TW200900512A - Method for fabricating aluminum alloy thick plate and aluminum alloy thick plate - Google Patents

Method for fabricating aluminum alloy thick plate and aluminum alloy thick plate Download PDF

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Publication number
TW200900512A
TW200900512A TW097111205A TW97111205A TW200900512A TW 200900512 A TW200900512 A TW 200900512A TW 097111205 A TW097111205 A TW 097111205A TW 97111205 A TW97111205 A TW 97111205A TW 200900512 A TW200900512 A TW 200900512A
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Taiwan
Prior art keywords
mass
aluminum alloy
less
alloy
thick plate
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TW097111205A
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Chinese (zh)
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TWI383053B (en
Inventor
Kazunori Kobayashi
Kenji Tokuda
Tomoharu Kato
Takashi Inaba
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Kobe Steel Ltd
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Priority claimed from JP2007095423A external-priority patent/JP4231530B2/en
Priority claimed from JP2007095419A external-priority patent/JP4231529B2/en
Priority claimed from JP2007098495A external-priority patent/JP4242429B2/en
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Publication of TW200900512A publication Critical patent/TW200900512A/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B21/00—Obtaining aluminium
    • C22B21/06—Obtaining aluminium refining
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D43/00—Mechanical cleaning, e.g. skimming of molten metals
    • B22D43/001—Retaining slag during pouring molten metal
    • B22D43/004—Retaining slag during pouring molten metal by using filtering means
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B21/00—Obtaining aluminium
    • C22B21/06—Obtaining aluminium refining
    • C22B21/066—Treatment of circulating aluminium, e.g. by filtration
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
    • C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
    • C22B9/02—Refining by liquating, filtering, centrifuging, distilling, or supersonic wave action including acoustic waves
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Acoustics & Sound (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Casting Support Devices, Ladles, And Melt Control Thereby (AREA)
  • Continuous Casting (AREA)

Abstract

The present invention provides a method for fabricating aluminum alloy thick plate, which is characterized that a dissolution step (S1) of dissolving aluminum alloy comprising a predetermined quantity of Mg, at least one kind of Si, Fe, Cu, Mn, Cr, Zn, Ti and Zr, and Al and an unavoidable impurities as a reminder, a dehydrogenation step (S2) of degassing hydrogen gas from the dissolved aluminum alloy, a filtration step (S3) of removing inclusion from the dehydrogenerated aluminum alloy, a casting step (S4) of casting the aluminum alloy with the inclusion removed to produce an ingot, a slicing step (S5) of slicing the ingot with a predetermined thickness to produce the aluminum alloy thick plate, and a heat treatment step (S6) of heating the aluminum alloy thick plate of predetermined thickness by retaining it in the temperature more than 400DEG C and less than melting point for more than an hour, are conducted in this order.

Description

200900512 九、發明說明 【發明所屬之技術領域】 本發明係關於錦合金厚板之製造方法以及銘合金厚 板。 【先前技術】 一般而目’銘合金厚板等的銘合金材，是使用於各種 用途。例如包括·底基板、搬送裝置、真空裝置用室等的 半導體相關裝置；電機電子元件及其製造裝置；生活用 品；機械零件等等。 這種鋁合金材，一般是如下述般製造出。亦即，將原 料之鋁合金經熔解、鑄造而製造出鑄塊，視需要進行均質 化熱處理’然後將該鑄塊壓延成既定厚度（例如參照專利 文獻1的段落0037〜0045)。 又關於衝壓用模具所使用的模具材料，是採用以下的 材料。亦即’作爲量產生產用是採用鋼鐵、鑄鋼等，作爲 試作用是採用鋅合金鑄物材、鋁合金鑄物材等等。又在近 幾年來’由於有多品種少量化的傾向，作爲中少量生產 用’鋁合金的壓延材、锻造材等的拉伸材已開始普及。 專利文獻1 :日本特開20〇5_344 1 73號公報 【發明內容】 然而，前述利用壓延之鋁合金材的製造方法，存在著 以下所示的問題。 -5- 200900512 (1 )在鑄造後進行壓延的方法，關於壓延板的表面 狀態及平坦度（特別是長邊方向的平坦度），僅是利用壓 延輥來進行，又經由熱壓延會在壓延板表面形成厚的氧化 皮膜，因此要控制表面狀態及平坦度會有困難。 (2)由於壓延輥不容易控制板厚，要謀求板厚精度 的提昇會有困難。又在板厚方向的中央部，由於金屬間化 合物的尺寸變大，在實施氧化鋁膜（alumite )處理的情 形，在板厚方向的截面及表面容易發生不均勻。又在將鑄 塊施以壓延的情形，隨著壓延次數增加會造成作業步驟增 加，而導致成本增高。 本發明是有鑑於前述課題而構成者，其目的是提供一 種具有優異的生產性、容易控制表面狀態及平坦度、且可 提昇板厚精度之鋁合金厚板之製造方法；並提供一種表面 狀態、平坦度及板厚精度優異之鋁合金厚板。 本申請的第1發明，係從鋁合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金，係含有Mg: 1.5質量％ 〜12.0質量％，且含有選自Si: 0·7質量。/。以下、Fe: 0.8 質量％以下、Cu : 0.6質量％以下、Μη : 1.0質量％以下、 Cr ·· 0.5質量％以下、Ζη ·· 0.4質量％以下、Ti ·· 0.1質量％ 以下、Zr : 0.3質量％以下中之至少1種，剩餘部分爲A1 及不可避免的雜質所構成；並且是依序進行以下步驟：將 前述鋁合金溶解的熔解步驟、從熔解後的鋁合金除去氫氣 之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜物之過濾 步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 -6- 200900512 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切割步 驟、將既定厚度的鋁合金厚板以400°C以上未達熔點的溫 度保持1小時以上來進行熱處理之熱處理步驟。 本申請的第2發明’係從銘合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金，係含有Μη: 0.3質量％ 〜1.6質量％，且含有選自Si: 0.7質量％以下、Fe: 0.8 質量％以下、Cu : 0_5質量％以下、Mg : 1 _5質量％以下、 Cr : 0.3質量％以下、Zn : 0.4質量％以下、Ti : 0. 1質量％ 以下、Zr : 0 · 3質量％以下中之至少1種，剩餘部分爲A1 及不可避免的雜質所構成；並且是依序進行以下步驟：將 前述鋁合金熔解的熔解步驟、從熔解後的鋁合金除去氫氣 之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜物之過濾 步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切割步 驟、將既定厚度的鋁合金厚板以400 °C以上未達熔點的溫 度保持1小時以上來進行熱處理之熱處理步驟。 本申請的第3發明，係從鋁合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金，係含有Si : 0.2質量％ 〜1 · 6質量％、M g : 〇. 3質量％〜1 . 5質量％，且含有選自 Fe: 0.8質量％以下、Cu: 1.0質量％以下、Μη: 0.6質量 %以下、Cr : 0.5質量％以下、Zn : 0.4質量％以下、Ti : 0.1質量％以下、Zr : 0.3質量％以下中之至少1種，剩餘 部分爲A1及不可避免的雜質所構成；並且是依序進行以 下步驟：將前述鋁合金熔解的熔解步驟、從熔解後的鋁合 200900512 金除去氫氣之脫氫氣步驟、從除去氫氣後的鋁合金除去夾 雜物之過濾步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之 鑄造步驟、將前述鑄塊切割而製造成既定厚度的鋁合金厚 板之切割步驟、將既定厚度的鋁合金厚板以400°c以上未 達溶點的溫度保持1小時以上來進行熱處理之熱處理步 驟。 本申請的第4發明，係從鋁合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金，係含有Mg : 0.4質量％ 〜4.0質量％、Zn: 3.0質量％〜9.0質量％，且含有選自 Si : 0.7質量％以下、Fe : 0.8質量％以下、Cu : 3.0質量％ 以下、Μη : 0.8質量％以下' Cr : 0.5質量％以下、Ti : 0.1 質量％以下、Zr : 0.25質量％以下中之至少1種，剩餘部 分爲A1及不可避免的雜質所構成；並且是依序進行以下 步驟：將前述鋁合金熔解的熔解步驟、從熔解後的鋁合金 除去氫氣之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜 物之過濾步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄 造步驟、將前述鑄塊切割而製造成既定厚度的鋁合金厚板 之切割步驟、將既定厚度的鋁合金厚板以350。(：以上未達 熔點的溫度保持1小時以上來進行熱處理之熱處理步驟。 在前述第1至第4發明中’較佳爲採用以下構成。 (A)在前述熱處理步驟後，進行表面平滑化處理步 驟’以對鋁合金厚板的表面實施表面平滑化處理。在此構 成中’前述表面平滑化處理較佳爲，以選自切削法、磨削 法及硏磨法中之1種以上的方法來進行。 -8 - 200900512 (B)在前述切割步驟中，將厚度方向中央部分從前 述鑄塊除去；該厚度方向中央部分，是從厚度方向中央朝 厚度方向之各表面具有均等的厚度，且設前述鑄塊厚度爲 T的情形，合計具有T/30〜T/5的厚度。 本申請的第5發明，係從鋁合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金，係含有Mg: 1.5質量％ 〜12.0質量％，且含有選自Si: 0.7質量％以下、Fe: 0.8 質量％以下、Cu : 0.6質量％以下、Μη : 1 ·0質量％以下、 C r : 0 · 5質量％以下、Ζη : 0 · 4質量％以下、T i : 0 · 1質量％ 以下、Zr : 0.3質量％以下中之至少1種，剩餘部分爲A1 及不可避免的雜質所構成；並且是依序進行以下步驟：將 前述鋁合金熔解的熔解步驟、從熔解後的鋁合金除去氫氣 之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜物之過濾 步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊以20(TC以上未達400°C的溫度保持1小時以 上來進行熱處理之熱處理步驟、將熱處理後的鑄塊切割而 製造成既定厚度的鋁合金厚板之切割步驟。 本申請的第6發明，係從鋁合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金’係含有Μη : 0.3質量％ 〜1.6質量％，且含有選自Si : 0.7質量％以下、Fe : 0.8 質量％以下、C u : 0.5質量％以下、M g : 1 . 5質量％以下、 C r : 0.3質量％以下、Ζ η : 0.4質量％以下、T i : 0 _ 1質量％ 以下、Zr : 0.3質量％以下中之至少1種’剩餘部分爲A1 及不可避免的雜質所構成；並且是依序進行以下步驟：將 -9- 200900512 前述鋁合金熔解的熔解步驟、從熔解後的鋁合金 之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜 步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄 將前述鑄塊以200°C以上未達400°C的溫度保持 上來進行熱處理之熱處理步驟、將熱處理後的鑄 製造成既定厚度的鋁合金厚板之切割步驟。 本申請的第7發明，係從鋁合金製造出鋁合 方法，其特徵在於：前述鋁合金，係含有Si: 0 〜1 . 6質量％、M g : 0.3質量％〜1 . 5質量％，且 Fe : 0.8質量％以下、Cu : 1 .0質量％以下、Μη : %以下、C r : 0.5質量％以下、Ζ η : 0 · 4質量％以 0.1質量％以下、Zr : 0.3質量％以下中之至少1 部分爲A1及不可避免的雜質所構成；並且是依 下步驟：將前述鋁合金熔解的熔解步驟、從熔解 金除去氫氣之脫氫氣步驟、從除去氫氣後的鋁合 雜物之過濾步驟、將除去夾雜物後的鋁合金鑄造 鑄造步驟、將前述鑄塊以200°C以上未達400°C 持1小時以上來進行熱處理之熱處理步驟、將熱 鑄塊切割而製造成既定厚度的鋁合金厚板之切割表 本申請的第8發明，係從鋁合金製造出銘合 方法，其特徵在於：前述鋁合金’係含有Mg: 0 〜4 · 0質量％、Ζ η : 3.0質量％〜9 · 0質量％ ’且 S i : 〇 · 7質量％以下、F e : 〇 · 8質量％以下、C u : 3 以下、Μ η : 0 _ 8質量％以下、C r : 0.5質量％以下 除去氫氣 物之過濾 造步驟、 1小時以 塊切割而 金厚板的 .2質量％ 含有選自 0.6質量 下 ' Ti : 種，剩餘 序進行以 後的鋁合 金除去夾 成鑄塊之 的溫度保 處理後的 泛驟。 金厚板的 .4質量％ 含有選自 .〇質量％ 、Ti : 0.1 -10- 200900512 質量％以下、z r : ο . 2 5質量％以下中之至少1種，剩餘部 分爲A1及不可避免的雜質所構成；並且是依序進行以下 步驟：將前述鋁合金熔解的熔解步驟、從熔解後的鋁合金 除去氫氣之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜 物之過濾步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄 造步驟、將前述鑄塊以200°C以上未達350°C的溫度保持1 小時以上來進行熱處理之熱處理步驟、將熱處理後的鑄塊 切割而製造成既定厚度的鋁合金厚板之切割步驟。 在前述第5至第8發明中，較佳爲採用以下構成。 (C )在前述切割步驟後，進行表面平滑化處理步 驟，以對既定厚度的鋁合金厚板的表面實施表面平滑化處 理。在此構成中，前述表面平滑化處理較佳爲，以選自切 削法、磨削法及硏磨法中之1種以上的方法來進行。 (D)在前述切割步驟中，將厚度方向中央部分從前 述鑄塊除去；該厚度方向中央部分，是從厚度方向中央朝 厚度方向之各表面具有均等的厚度’且設前述鑄塊厚度爲 T的情形，合計具有T/30〜T/5的厚度。 本申請的第9發明’係從鋁合金製造出鋁合金厚板的 方法，其特徵在於：前述鋁合金’係含有Mg: 1.5質量％ 〜12.0質量％，且含有選自Si : 0.7質量％以下、Fe : 0.8 質量％以下、C u : 〇 6質量％以下、Μ η : 1.0質量％以下、 Cr : 0.5質量％以下、Ζη : 〇·4質量％以下、Ti : 〇·1質量％ 以下、Zr : 0.3質量％以下中之至少1種，剩餘部分爲A1 及不可避免的雜質所構成；並且是依序進行以下步驟：將 -11 - 200900512 前述鋁合金熔解的熔解步驟、從熔解後的鋁合金除去氫 之脫氫氣步驟、從除去氫氣後的銘合金除去夾雜物之過 步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切割 驟、將既定厚度的鋁合金厚板以200 °C以上未達400°C 溫度保持1小時以上來進行熱處理之熱處理步驟。 本申請的第1 0發明，係從鋁合金製造出鋁合金厚 的方法，其特徵在於：前述鋁合金，係含有Μη: 0.3質 %〜1.6質量％，且含有選自Si : 0.7質量％以下、Fe :( 質量％以下、C u : 0.5質量％以下、M g : 1 · 5質量％以下 Cr : 0.3質量％以下、Zn : 0.4質量％以下、Ti : 0.1質量 以下、Zr : 0.3質量％以下中之至少1種，剩餘部分爲 及不可避免的雜質所構成；並且是依序進行以下步驟： 前述鋁合金熔解的熔解步驟、從熔解後的鋁合金除去氫 之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜物之過 步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切割 驟、將既定厚度的鋁合金厚板以2〇〇°C以上未達400 °C 溫度保持1小時以上來進行熱處理之熱處理步驟。 本申請的第1 1發明，係從鋁合金製造出鋁合金厚 的方法，其特徵在於：前述鋁合金，係含有Si : 0.2質 %〜1 . 6質量％、M g : 0 · 3質量％〜1 · 5質量％，且含有選 F e : 〇 . 8質量％以下、C u : 1.0質量％以下、Μ η : 0 _ 6質 %以下、Cr : 0.5質量％以下、Ζη : 0.4質量％以下、Ti 氣 濾 步 的 板 量 L8 、 % A1 將 氣 濾 步 的 板 且 里 白 量 -12 - 200900512 〇· 1質量％以下、Zr : 0.3質量％以下中之至少1種’剩餘 部分爲A1及不可避免的雜質所構成；並且是依序進行以 下步驟：將前述鋁合金熔解的熔解步驟、從熔解後的鋁合 金除去氫氣之脫氫氣步驟、從除去氫氣後的鋁合金除去夾 雜物之過濾步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之 鑄造步驟、將前述鑄塊切割而製造成既定厚度的銘合金厚 板之切割步驟、將既定厚度的鋁合金厚板以200°C以上未 達400 °C的溫度保持1小時以上來進行熱處理之熱處理步 驟。 本申請的第12發明，係從鋁合金製造出鋁合金厚板 的方法，其特徵在於：前述鋁合金，係含有Mg : 0.4質量 〇/。〜4.0質量％、Zn : 3.0質量％〜9.0質量％，且含有選自 Si : 0.7質量％以下、Fe : 0.8質量％以下、Cu : 3.0質量％ 以下、Μη: 0.8質量％以下、Cr: 0.5質量°/〇以下、Ti: 0_1 質量％以下、Zr : 0.2 5質量％以下中之至少1種’剩餘部 分·爲A1及不可避免的雜質所構成；並且是依序進行以下 步驟：將前述銘合金熔解的熔解步驟、從熔解後的鋁合金 _去氫氣之脫氫氣步驟、從除去氫氣後的鋁合金除去夾雜 牧/之過濾步驟、將除去夾雜物後的鋁合金鑄造成鑄塊之鑄 g步驟、將前述鑄塊切割而製造成既定厚度的鋁合金厚板 之切割步驟、將既定厚度的鋁合金厚板以2 00 °C以上未達 3 50。(：的溫度保持1小時以上來進行熱處理之熱處理步 驟。 在前述第9至第12發明中，較佳爲採用以下構成。 -13- 200900512 (E )在前述熱處理步驟後，進行表面平滑化處 驟，以對鋁合金厚板的表面實施表面平滑化處理。在 成中，前述表面平滑化處理較佳爲，以選自切削法、 法及硏磨法中之1種以上的方法來進行。 (F)在前述切割步驟中，將厚度方向中央部分 述鑄塊除去；該厚度方向中央部分，是從厚度方向中 厚度方向之各表面具有均等的厚度，且設前述鑄塊厚 T的情形，合計具有T/30〜T/5的厚度。 本申請的第1 3發明，其特徵在於：係藉由前述 至第12發明之任一鋁合金厚板之製造方法所製造出 合金厚板，且具有400 // m以下的平均結晶粒徑。 在前述第1至第4發明中，由於將鋁合金的既定 的含量限定在既定範圍，能提昇鋁合金厚板的金屬間 物的微細化及強度。又由於藉由脫氫氣步驟來除去氫 可限定鑄塊中的氫濃度，即使鑄塊中的結晶粒粗大化 不會在鑄塊表面附近的粒界發生氫的集積、濃化’可 鑄塊的鼓起，並抑制起因於鼓起之鋁合金厚板的捲起 能抑制會形成厚板的表面缺陷之厚板表面的潛在缺陷 能提昇鋁合金厚板的強度。又藉由過濾步驟來從銘合 去氧化物和非金屬等的夾雜物。又藉由切割步驟來切 塊，因此可減少氧化皮膜厚度，且提昇鋁合金厚板的 狀態、平坦度及板厚精度’又能提昇生產性。再者， 熱處理步驟來對鋁合金厚板實施熱處理’因此可除去 應力，又能使內部組織均一化。 理步 此構 磨削 從前 央朝 度爲 第1 之鋁 元素 化合 氣， ，仍 抑制 ，又 。又 金除 割鑄 表面 藉由 內部 -14- 200900512 因此，依據前述第1至第4發明，可提昇鋁合金厚板 的強度。又由於將鑄塊切割來製造成鋁合金厚板，不須像 習知般藉由熱壓延來減少厚度，能謀求作業步驟的省略 化，因此可提昇生產性。又能抑制厚板的表面及截面之不 均勻（色調不均勻），可提昇平坦度、氧化鋁膜處理後的 外觀性狀、板厚精度。又由於對切割後之既定厚度的鋁合 金厚板以400 °C (或35(TC )至未達熔點的溫度實施熱處 理，可除去內部應力並謀求內部組織的均一化，可獲得良 好的平坦度及板厚精度，又能維持強度。 依據前述構成（A)，可進一步提昇鋁合金厚板之表 面狀態及平坦度。又藉由表面平滑化，厚板表面之氣體堆 積消失，當鋁合金厚板應用於真空裝置用室的情形，可提 昇室的真空度。 依據前述構成（B )，係將氧化鋁膜處理後之鋁合金 厚板的表面和截面之容易發生不均勻的鑄塊中央部分除 去，因此可獲得，在氧化鋁膜處理後仍具有優異的外觀性 之銘合金厚板。又能減少批次內的參差情形。 在前述第5至第8發明中，由於將鋁合金的既定元素 的含量限定在既定範圍，能提昇鋁合金厚板的金屬間化合 物的微細化及強度。又由於藉由脫氫氣步驟來除去氫氣’ 可限定鑄塊中的氫濃度，即使鑄塊中的結晶粒粗大化’仍 不會在鑄塊表面附近的粒界發生氫的集積、濃化’可抑制 鑄塊的鼓起，並抑制起因於鼓起之鋁合金厚板的捲起’又 能抑制會形成厚板的表面缺陷之厚板表面的潛在缺陷°又 -15- 200900512 能提昇鋁合金厚板的強度。又藉由過濾步驟來從鋁合金除 去氧化物和非金屬等的夾雜物。且藉由熱處理步驟來對鑄 塊實施熱處理，因此可除去內部應力，又能使內部組織均 一化。又藉由切割步驟來切割鑄塊，因此可減少氧化皮膜 厚度，且提昇鋁合金厚板的表面狀態、平坦度及板厚精 度，而能提昇生產性。 因此，依據前述第5至第8發明，可提昇鋁合金厚板 之平坦度、強度及切削性間的均衡。亦即，由於對鑄塊以 2 00 °C以上未達400°C (或3 5 0 °C )的溫度實施熱處理，可 防止延展性變高，因此不會使切削性（切削斷裂性）變 差，而能謀求內部應力的除去及內部組織的均一化。因 此，可實現良好的平坦度及板厚精度。又能維持強度。又 由於將鑄塊切割而製造成鋁合金厚板，不須像習知般藉由 熱壓延來減少厚度，能謀求作業步驟的省略化，因此可提 昇生產性。又能抑制厚板截面的表面之不均勻（色調不均 勻），可提昇平坦度、氧化鋁膜處理後的外觀性狀、板厚 精度。 依據前述構成（C)，可進一步提昇鋁合金厚板之表 面狀態及平坦度。又藉由表面平滑化，厚板表面之氣體堆 積消失，當鋁合金厚板應用於真空裝置用室的情形，可提 昇室的真空度。 依據前述構成（D )，係將氧化鋁膜處理後之鋁合金 厚板的表面和截面之容易發生不均勻的鑄塊中央部分除 去’因此可獲得，在氧化鋁膜處理後仍具有優異的外觀性 -16- 200900512 之鋁合金厚板。又能減少批次內的參差情形。 在前述第9至第12發明中，由於將鋁合金的既定元 素的含量限定在既定範圍，能提昇鋁合金厚板的金屬間化 合物的微細化及強度。又由於藉由脫氫氣步驟來除去氫 氣，可限定鑄塊中的氫濃度，即使鑄塊中的結晶粒粗大 化，仍不會在鑄塊表面附近的粒界發生氫的集積、濃化， 可抑制鑄塊的鼓起，並抑制起因於鼓起之鋁合金厚板的捲 起，又能抑制會形成厚板的表面缺陷之厚板表面的潛在缺 陷。又能提昇鋁合金厚板的強度。又藉由過濾步驟來從鋁 合金除去氧化物和非金屬等的夾雜物。又藉由切割步驟來 切割鑄塊，因此可減少氧化皮膜厚度’且提昇鋁合金厚板 的表面狀態、平坦度及板厚精度，又能提昇生產性。再 者，藉由熱處理步驟來對鋁合金厚板實施熱處理，因此可 除去內部應力，又能使內部組織均一化。 因此，依據前述第9至第12發明’可提昇鋁合金厚 板的強度。又由於將鑄塊切割來製造成鋁合金厚板’不須 像習知般藉由熱壓延來減少厚度’能謀求作業步驟的省略 化，因此可提昇生產性。又能抑制厚板的表面及截面之不 均勻（色調不均勻）’可提昇平坦度、氧化鋁膜處理後的 外觀性狀、板厚精度。又能提昇鋁合金厚板之平坦度、強 度及切削性間的均衡。亦即’由於對鑄塊以2 0 0 °C以上未 達400 °C (或350 °C)的溫度實施熱處理’可防止延展性 變高，因此不會使切削性（切削斷裂性）變差’而能謀求 內部應力的除去及內部組織的均一化。因此’可實現良好 -17- 200900512 的平坦度及板厚精度。又能維持強度。 依據前述構成（E)，可進一步提昇鋁合金厚板之表 面狀態及平坦度。又藉由表面平滑化，厚板表面之氣體堆 積消失，當鋁合金厚板應用於真空裝置用室的情形，可提 昇室的真空度。 依據前述構成（F )，係將氧化鋁膜處理後之鋁合金 厚板的表面和截面之容易發生不均勻的鑄塊中央部分除 去，因此可獲得，在氧化鋁膜處理後仍具有優異的外觀性 之鋁合金厚板。又能減少批次內的參差情形。 依據前述第1 3發明，可獲得優異的表面狀態、平坦 度及板厚精度。又藉由表面平滑化處理能使氣體堆積消 失，而獲得高品質。再者，由於在氧化鋁膜處理後之表面 外觀幾乎不會發生不均勻，可應用於各式各樣的用途，也 能回收使用於其他用途。 【實施方式】 參照圖式來詳細說明本發明的鋁合金厚板之製造方法 及銘合金厚板。在此，將本申請的發明分成（A)第1至 第4發明、（B)第5至第8發明、（C)第9至第12發 明以及（D )第丨3發明來做說明。 (A)第1至第4發明之鋁合金厚板之製造方法 (1 )製造方法之槪要 第1至第4發明之鋁合金厚板（以下也稱爲「厚 -18- 200900512 板」）之製造方法，如第1圖所示，係依序進行 驟（S1 )、脫氫氣步驟（S2 )、過濾步驟（S3 ) 驟（S 4 )、切割步驟（s 5 )、熱處理步驟（s 6 ) 要’可在熱處理步驟（s 6 )後進行表面平滑化 (S7 )。 在本製造方法，首先，將原料之鋁合金厚板 驟（S 1 )進行熔解。接著，從熔解後的鋁合金中 氫氣步驟（S2)來除去氫氣。接著，藉由過濾步 來除去氧化物和非金屬等的夾雜物。接著，該鋁 鑄造步驟（S4 )鑄造成鑄塊。然後，該鑄塊在 (S 5 )進行切割而形成既定厚度的鋁合金厚板。 既定厚度的鋁合金厚板藉由熱處理步驟（S6) 理，接著，按照需要，藉由表面平滑化處理步驟 進行表面平滑化處理。 (2 )銘合金 在第1至第4發明之製造方法，作爲原料之 係分別使用5000系之Al-Mg合金，3000系之 金，6000系之Al-Mg-Si系合金以及7000系之 合金。具體內容說明如下。 (2 -1 )第1發明 使用5000系之Al-Mg合金。該鋁合金含有 質量％〜12.0質量％ ’且含有選自Si: 0.7質量 :熔解步 、鐘造步 。又視需 處理步驟 在熔解步 ，藉由脫 驟（S3) 合金是在 切割步驟 然後，將 進行熱處 (S7 )來 金吕合金， Al-Mn 合 A1 - Z η - M g200900512 IX. Description of the Invention [Technical Field of the Invention] The present invention relates to a method for producing a slab of a slab alloy and a slab of an alloy. [Prior Art] The general alloy materials such as the alloy plate and the like are used for various purposes. For example, a semiconductor-related device including a base substrate, a transfer device, a vacuum device chamber, a motor electronic component and a manufacturing device thereof, a living product, a mechanical component, and the like. Such an aluminum alloy material is generally produced as follows. That is, the aluminum alloy of the raw material is melted and cast to produce an ingot, and if necessary, a homogenization heat treatment is performed. Then, the ingot is calendered to a predetermined thickness (for example, refer to paragraphs 0037 to 0045 of Patent Document 1). Further, regarding the mold material used for the die for press, the following materials are used. That is to say, steel is used as a quantity, steel, cast steel, etc., and zinc alloy cast materials, aluminum alloy cast materials, and the like are used as test effects. Further, in recent years, there has been a tendency to reduce the amount of the product, and it has been popularized as a rolled material such as a rolled material or a forged material of a small amount of aluminum alloy. [Patent Document 1] Japanese Laid-Open Patent Publication No. Hei. No. Hei. No. Hei. -5- 200900512 (1) The method of rolling after casting, regarding the surface state and flatness of the rolled sheet (especially the flatness in the longitudinal direction), is performed only by the calender roll, and is also subjected to hot calendering. A thick oxide film is formed on the surface of the rolled sheet, so it is difficult to control the surface state and flatness. (2) Since the calender roll does not easily control the thickness of the sheet, it is difficult to improve the sheet thickness accuracy. Further, in the central portion in the thickness direction, the size of the intermetallic compound is increased, and in the case of performing alumite treatment, the cross section and the surface in the thickness direction are likely to be uneven. Further, in the case where the cast block is subjected to rolling, as the number of rolling increases, the number of work steps is increased, resulting in an increase in cost. The present invention has been made in view of the above problems, and an object thereof is to provide a method for manufacturing an aluminum alloy thick plate which has excellent productivity, can easily control surface state and flatness, and can improve plate thickness precision, and provides a surface state. Aluminum alloy thick plate with excellent flatness and plate thickness accuracy. The first invention of the present invention is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy contains Mg: 1.5% by mass to 12.0% by mass, and contains a mass selected from Si: 0·7. . /. Hereinafter, Fe: 0.8% by mass or less, Cu: 0.6% by mass or less, Μη: 1.0% by mass or less, Cr··0.5% by mass or less, Ζη··0.4% by mass or less, Ti··0.1% by mass or less, Zr: 0.3 At least one of mass % or less, the remainder being composed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of dissolving the aluminum alloy, and a dehydrogenation step of removing hydrogen from the molten aluminum alloy a step of removing the inclusions from the aluminum alloy after removing the hydrogen gas, a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, -6-200900512 cutting the ingot to produce an aluminum alloy thick plate having a predetermined thickness The step of cutting, heat-treating the aluminum alloy thick plate of a predetermined thickness at a temperature of 400 ° C or more and not reaching the melting point for 1 hour or more to perform heat treatment. In the second invention of the present application, a method for producing an aluminum alloy thick plate from the alloy is characterized in that the aluminum alloy contains Μη: 0.3% by mass to 1.6% by mass and contains Si: 0.7% by mass or less. Fe: 0.8% by mass or less, Cu: 0_5 mass% or less, Mg: 1 _5 mass% or less, Cr: 0.3 mass% or less, Zn: 0.4 mass% or less, Ti: 0.1 mass% or less, Zr: 0 At least one of 3 mass% or less, the remainder being composed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting the aluminum alloy, and a hydrogen removal process for removing hydrogen from the molten aluminum alloy a step of removing the inclusions from the aluminum alloy after removing the hydrogen gas, a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, and a step of cutting the ingot by cutting the ingot to produce a thick aluminum alloy plate having a predetermined thickness A heat treatment step of heat-treating the aluminum alloy thick plate of a predetermined thickness at a temperature of 400 ° C or more and less than the melting point for 1 hour or more. The third invention of the present invention is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy contains Si: 0.2% by mass to 1.6% by mass, and M g : 〇. 3 % by mass ～5% by mass and containing Fe: 0.8% by mass or less, Cu: 1.0% by mass or less, Μη: 0.6% by mass or less, Cr: 0.5% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1 mass % or less, Zr: at least one of 0.3% by mass or less, the remainder being composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: a melting step of melting the aluminum alloy, and an aluminum alloy after melting 200900512 Gold removal process for dehydrogenation of hydrogen, filtration step for removing inclusions from aluminum alloy after removal of hydrogen, casting step of casting aluminum alloy into ingot after removing inclusions, cutting the ingot to produce a predetermined thickness The step of cutting the aluminum alloy thick plate, and heat-treating the aluminum alloy thick plate of a predetermined thickness at a temperature of 400 ° C or more and not reaching the melting point for 1 hour or more. The fourth invention of the present invention is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy contains Mg: 0.4% by mass to 4.0% by mass, and Zn: 3.0% by mass to 9.0% by mass. Further, it is selected from Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 3.0% by mass or less, Μη: 0.8% by mass or less, 'Cr: 0.5% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.25 mass. At least one of % or less, the remainder being composed of A1 and unavoidable impurities; and sequentially performing the following steps: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, a step of removing the inclusions from the aluminum alloy after removing the hydrogen, a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, and a step of cutting the ingot to produce a thick aluminum alloy plate having a predetermined thickness, and The thickness of the aluminum alloy plate is 350. (The heat treatment step in which the temperature of the melting point is not maintained for 1 hour or more and heat treatment is performed. In the first to fourth inventions described above, it is preferable to adopt the following configuration. (A) After the heat treatment step, surface smoothing treatment is performed. In the step of performing the surface smoothing treatment on the surface of the aluminum alloy thick plate, in the above configuration, the surface smoothing treatment is preferably one or more selected from the group consisting of a cutting method, a grinding method, and a honing method. -8 - 200900512 (B) In the cutting step, the central portion in the thickness direction is removed from the ingot; the central portion in the thickness direction has an equal thickness from the center in the thickness direction toward each surface in the thickness direction, and In the case where the thickness of the ingot is T, the thickness is T/30 to T/5. The fifth invention of the present invention is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy is Mg: 1.5% by mass to 12.0% by mass, and containing Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.6% by mass or less, Μη: 1·0% by mass or less, Cr: 0 · 5 quality % or less, Ζη : 0 · 4 mass % or less, T i : 0 · 1 mass % or less, Zr: 0.3 mass % or less, at least one of them, and the remainder is composed of A1 and unavoidable impurities; The following steps are performed: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, a filtration step of removing inclusions from the aluminum alloy after removing the hydrogen, and casting the aluminum alloy from which the inclusions are removed The casting step of the ingot, the heat treatment step of heat-treating the ingot by holding the ingot at a temperature of not more than 400 ° C for 1 hour or more, and cutting the ingot after the heat treatment to produce an aluminum alloy thick plate having a predetermined thickness The sixth invention of the present invention is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy' contains Μη: 0.3% by mass to 1.6% by mass, and contains a selected from Si: 0.7% by mass or less, Fe: 0.8% by mass or less, C u : 0.5% by mass or less, M g : 1.5% by mass or less, C r : 0.3% by mass or less, Ζ η : 0.4% by mass or less, T i : 0 _ 1 quality In the following, at least one of Zr: 0.3% by mass or less is formed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting the aluminum alloy of -9-200900512, after melting Dehydrogenation step of aluminum alloy, removal of inclusion step from aluminum alloy after removal of hydrogen, casting of aluminum alloy after removal of inclusions into ingot, casting the ingot at a temperature of 200 ° C or more and less than 400 ° C A heat treatment step of performing heat treatment, and a step of cutting the heat-treated cast into an aluminum alloy thick plate having a predetermined thickness. According to a seventh aspect of the invention, there is provided a method for producing an aluminum alloy from an aluminum alloy, characterized in that the aluminum alloy contains Si: 0 to 1.6% by mass, and Mg: 0.3% by mass to 1.5% by mass. Further, Fe: 0.8% by mass or less, Cu: 1.0% by mass or less, Μη: % or less, Cr: 0.5% by mass or less, Ζ η: 0 · 4% by mass, 0.1% by mass or less, and Zr: 0.3% by mass or less At least one of the components is composed of A1 and unavoidable impurities; and the following steps are: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten gold, and an aluminum complex after removing the hydrogen a step of filtering, an aluminum alloy casting and casting step of removing the inclusions, a heat treatment step of heat-treating the ingot at 200 ° C or more and less than 400 ° C for 1 hour or more, and cutting the hot ingot to have a predetermined thickness The eighth invention of the present invention is a method for producing a molding method from the aluminum alloy, characterized in that the aluminum alloy ' contains Mg: 0 to 4 · 0 mass %, Ζ η : 3.0 mass %~9 · 0% by mass 'and S i : 〇· 7 quality % or less, F e : 〇 · 8 mass % or less, C u : 3 or less, η η : 0 _ 8 mass % or less, C r : 0.5 mass % or less, a filtration step of removing a hydrogen gas, and a block cutting by one hour The .2 mass% of the gold plate contains a general temperature after the temperature-protection treatment of the aluminum alloy selected from 0.6 masses of 'Ti: the remaining aluminum alloy is removed and the ingot is removed. The .4 mass% of the gold plate contains at least one selected from the group consisting of: 〇 mass%, Ti: 0.1 -10- 200900512 mass% or less, zr: ο. 25 mass% or less, and the remainder is A1 and inevitable. And consisting of the following steps: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, a filtration step of removing inclusions from the aluminum alloy after removing hydrogen, and removing A casting step of casting an aluminum alloy after inclusions into an ingot, a heat treatment step of heat-treating the ingot at a temperature of 200 ° C or more and less than 350 ° C for 1 hour or more, and cutting the ingot after heat treatment The cutting step of forming an aluminum alloy thick plate of a predetermined thickness. In the fifth to eighth inventions described above, it is preferable to adopt the following configuration. (C) After the aforementioned cutting step, a surface smoothing treatment step is performed to perform surface smoothing treatment on the surface of the aluminum alloy thick plate of a predetermined thickness. In the above configuration, the surface smoothing treatment is preferably carried out by one or more methods selected from the group consisting of a cutting method, a grinding method, and a honing method. (D) in the cutting step, the central portion in the thickness direction is removed from the ingot; the central portion in the thickness direction has a uniform thickness from the center in the thickness direction toward each surface in the thickness direction, and the thickness of the ingot is T In the case of a total, it has a thickness of T/30 to T/5. A ninth invention of the present application is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy' contains Mg: 1.5% by mass to 12.0% by mass, and contains Si: 0.7% by mass or less. Fe: 0.8% by mass or less, C u : 〇6 mass% or less, Μ η: 1.0 mass% or less, Cr: 0.5 mass% or less, Ζη: 〇·4 mass% or less, Ti: 〇·1 mass% or less, Zr: at least one of 0.3% by mass or less, the remainder being composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: a melting step of melting the aforementioned aluminum alloy of -11 - 200900512, from the molten aluminum a step of removing hydrogen from the alloy to remove hydrogen, a step of removing inclusions from the alloy after removing the hydrogen, and a step of casting the aluminum alloy from which the inclusions are removed into an ingot, and cutting the ingot to produce an aluminum alloy having a predetermined thickness A step of cutting a thick plate, and heat-treating the aluminum alloy thick plate of a predetermined thickness at a temperature of 200 ° C or more and less than 400 ° C for 1 hour or more. A tenth invention of the present invention is a method for producing an aluminum alloy from an aluminum alloy, characterized in that the aluminum alloy contains Μη: 0.3% by mass to 1.6% by mass and contains Si: 0.7% by mass or less. , Fe : (% by mass or less, C u : 0.5% by mass or less, M g : 1 · 5 mass % or less, Cr: 0.3% by mass or less, Zn: 0.4% by mass or less, Ti: 0.1 or less, and Zr: 0.3% by mass At least one of the following, the remainder being composed of unavoidable impurities; and the following steps are sequentially performed: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, and removing hydrogen from the molten metal After the step of removing the inclusions from the aluminum alloy, and casting the aluminum alloy after the inclusions are cast into the ingot, the ingot is cut to produce a cutting step of the aluminum alloy thick plate of a predetermined thickness, and the aluminum of a predetermined thickness is formed. The heat treatment step of heat-treating the alloy thick plate at a temperature of 2 ° C or more and less than 400 ° C for 1 hour or more. The first invention of the present application is a method for producing an aluminum alloy thick from an aluminum alloy, characterized in that The aluminum alloy contains Si: 0.2% by mass to 1.6% by mass, M g : 0 · 3 mass% to 1 · 5 mass%, and contains F e : 〇. 8 mass% or less, C u : 1.0% by mass or less, Μ η: 0 _ 6 mass% or less, Cr: 0.5 mass% or less, Ζη: 0.4 mass% or less, plate amount L8 of the gas filtration step, and % A1 -12 - 200900512 至少·1 mass% or less, Zr: 0.3% by mass or less, at least one of which is composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: melting of the aforementioned aluminum alloy a step of removing hydrogen from the molten aluminum alloy, a step of removing inclusions from the aluminum alloy after removing hydrogen, a casting step of casting the aluminum alloy after removing the inclusions into an ingot, and cutting the ingot The heat treatment step of heat-treating the aluminum alloy thick plate having a predetermined thickness and maintaining the thickness of the aluminum alloy thick plate having a predetermined thickness at a temperature of 200 ° C or more and less than 400 ° C for 1 hour or more. Invention, made from aluminum alloy A method for producing an aluminum alloy thick plate, characterized in that the aluminum alloy contains Mg: 0.4 mass% / 4.0% by mass, Zn: 3.0 mass% - 9.0 mass%, and contains Si: 0.7 mass% or less , Fe: 0.8% by mass or less, Cu: 3.0% by mass or less, Μη: 0.8% by mass or less, Cr: 0.5 mass%/〇 or less, Ti: 0_1% by mass or less, and Zr: 0.25% by mass or less. 'The remaining part is composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: a melting step of melting the aforementioned alloy, a dehydrogenation step from the molten aluminum alloy to dehydrogenation, and a step of removing hydrogen from the hydrogen a step of filtering the aluminum alloy to remove the mixed grazing, a step of casting the aluminum alloy from which the inclusions are removed into an ingot, a step of cutting the ingot, and a step of cutting the aluminum alloy thick plate having a predetermined thickness, and a predetermined thickness The aluminum alloy thick plate is less than 3 50 at 200 °C or above. The heat treatment step of heat treatment is carried out for a temperature of 1 hour or more. In the above-described ninth to twelfth inventions, the following constitution is preferably employed. -13- 200900512 (E) After the heat treatment step, surface smoothing is performed. The surface smoothing treatment is performed on the surface of the aluminum alloy thick plate. The surface smoothing treatment is preferably carried out by one or more methods selected from the group consisting of a cutting method, a method, and a honing method. (F) in the cutting step, the ingot in the central portion in the thickness direction is removed; and the central portion in the thickness direction has a uniform thickness from each of the thickness directions in the thickness direction, and the thickness of the ingot is set to be T. In the third aspect of the invention, the alloy thick plate is produced by the method for producing an aluminum alloy thick plate according to any one of the above-described twelfth invention, and In the first to fourth inventions described above, since the predetermined content of the aluminum alloy is limited to a predetermined range, the fineness and strength of the intermetallic substance of the aluminum alloy thick plate can be improved. .also Since the removal of hydrogen by the dehydrogenation step can limit the concentration of hydrogen in the ingot, even if the crystal grains in the ingot are coarsened, hydrogen accumulation and concentration in the grain boundary near the surface of the ingot can be concentrated. And suppressing the potential defects caused by the rolling up of the thickened aluminum alloy thick plate to suppress the surface of the thick plate which will form a thick plate can enhance the strength of the aluminum alloy thick plate. Oxide and non-metallic inclusions are removed, and the cutting step is used to cut the block, thereby reducing the thickness of the oxide film and improving the state, flatness and thickness accuracy of the aluminum alloy thick plate, which can improve productivity. The heat treatment step is to heat-treat the aluminum alloy thick plate' so that the stress can be removed and the internal structure can be uniformized. The structure is ground from the front central direction to the first aluminum elemental gas, which is still suppressed, and Further, the gold removal cutting surface is internally 14-200900512. Therefore, according to the first to fourth inventions described above, the strength of the aluminum alloy thick plate can be improved, and the aluminum alloy thick plate can be manufactured by cutting the ingot. It is necessary to reduce the thickness by hot rolling as in the prior art, and it is possible to eliminate the work step, thereby improving productivity, suppressing unevenness of the surface and cross section of the thick plate (uneven color tone), and improving flatness. The appearance property and thickness accuracy of the aluminum oxide film after treatment, and the internal stress can be removed by heat-treating the aluminum alloy thick plate of a predetermined thickness after cutting at a temperature of 400 ° C (or 35 (TC ) to a temperature less than the melting point) In order to achieve uniformity of internal organization, good flatness and thickness accuracy can be obtained, and strength can be maintained. According to the above configuration (A), the surface state and flatness of the aluminum alloy thick plate can be further improved. The gas accumulation on the surface of the thick plate disappears, and when the aluminum alloy thick plate is applied to the chamber for the vacuum device, the vacuum degree of the chamber can be improved. According to the above configuration (B), the central portion of the ingot which is likely to be uneven in the surface and the cross section of the aluminum alloy thick plate after the alumite treatment is obtained, and thus it is obtained, and has an excellent appearance after the treatment of the aluminum oxide film. Sexuality alloy thick plate. It can also reduce the staggering situation in the batch. In the fifth to eighth inventions, since the content of the predetermined element of the aluminum alloy is limited to a predetermined range, the refinement and strength of the intermetallic compound of the aluminum alloy thick plate can be improved. Further, since the hydrogen gas is removed by the dehydrogenation step, the concentration of hydrogen in the ingot can be limited, and even if the crystal grains in the ingot are coarsened, "the accumulation and concentration of hydrogen at the grain boundary near the surface of the ingot" will not occur. Suppresses the bulging of the ingot and suppresses the roll-up of the aluminum alloy slab caused by the bulging, and can suppress the potential defects of the slab surface which will form the surface defects of the slab. -15- 200900512 can increase the thickness of the aluminum alloy The strength of the board. In addition, inclusions such as oxides and non-metals are removed from the aluminum alloy by a filtration step. Further, the heat treatment step is used to heat-treat the ingot, so that internal stress can be removed and the internal structure can be made uniform. Further, by cutting the ingot by the cutting step, the thickness of the oxide film can be reduced, and the surface state, flatness, and thickness of the aluminum alloy thick plate can be improved, and productivity can be improved. Therefore, according to the fifth to eighth inventions described above, the balance between the flatness, the strength, and the machinability of the aluminum alloy thick plate can be improved. In other words, since the heat treatment is performed on the ingot at a temperature of not more than 200 ° C (or 350 ° C), the ductility is prevented from becoming high, so that the machinability (cutting fracture property) is not changed. Poor, and the removal of internal stress and the homogenization of internal organization can be sought. Therefore, good flatness and thickness accuracy can be achieved. It can maintain strength. Further, since the ingot is cut and manufactured into an aluminum alloy thick plate, the thickness can be reduced by hot rolling as is conventionally known, and the work step can be omitted, so that productivity can be improved. Further, it is possible to suppress the unevenness of the surface of the thick plate section (uneven color tone), and to improve the flatness, the appearance property after the treatment of the aluminum oxide film, and the thickness accuracy. According to the above configuration (C), the surface condition and flatness of the aluminum alloy thick plate can be further improved. Further, by surface smoothing, the gas accumulation on the surface of the thick plate disappears, and when the aluminum alloy thick plate is applied to the chamber for the vacuum apparatus, the degree of vacuum of the chamber can be improved. According to the above configuration (D), the surface of the aluminum alloy thick plate after the alumite treatment and the cross-section of the central portion of the ingot which are liable to be uneven are easily removed. Therefore, it is obtained, and the aluminum film is treated to have an excellent appearance. Aluminium alloy thick plate of sex-16-200900512. It can also reduce the staggering situation in the batch. In the above-described ninth to twelfth inventions, since the content of the predetermined element of the aluminum alloy is limited to a predetermined range, the refinement and strength of the intermetallic compound of the aluminum alloy thick plate can be improved. Further, since the hydrogen gas is removed by the dehydrogenation step, the concentration of hydrogen in the ingot can be limited, and even if the crystal grains in the ingot are coarsened, hydrogen accumulation and concentration do not occur at the grain boundary near the surface of the ingot. The bulging of the ingot is suppressed, and the rolling up of the swelled aluminum alloy slab is suppressed, and the potential defect of the slab surface which will form the surface defect of the slab can be suppressed. It can also increase the strength of aluminum alloy thick plates. The inclusions such as oxides and non-metals are removed from the aluminum alloy by a filtration step. Further, by cutting the ingot by the cutting step, the thickness of the oxide film can be reduced, and the surface state, flatness, and thickness accuracy of the aluminum alloy thick plate can be improved, and productivity can be improved. Further, by heat-treating the aluminum alloy thick plate by heat treatment, the internal stress can be removed and the internal structure can be made uniform. Therefore, according to the above-described ninth to twelfth inventions, the strength of the aluminum alloy thick plate can be improved. Further, since the ingot is cut to produce an aluminum alloy thick plate, the thickness can be reduced by hot rolling without the need to reduce the work step, so that the workability can be improved. Further, it is possible to suppress the unevenness of the surface and the cross section of the thick plate (uneven color tone), which can improve the flatness, the appearance property after the treatment of the aluminum oxide film, and the thickness accuracy. It also improves the balance between flatness, strength and machinability of aluminum alloy thick plates. That is, 'heat treatment at a temperature of 200 ° C (or 350 ° C) above 200 ° C can prevent the ductility from becoming high, so the machinability (cutting fracture) is not deteriorated. 'It is possible to remove internal stress and homogenize internal organization. Therefore, it is possible to achieve good flatness and plate thickness accuracy of -17-200900512. It can maintain strength. According to the above configuration (E), the surface condition and flatness of the aluminum alloy thick plate can be further improved. Further, by surface smoothing, the gas accumulation on the surface of the thick plate disappears, and when the aluminum alloy thick plate is applied to the chamber for the vacuum apparatus, the degree of vacuum of the chamber can be improved. According to the above configuration (F), the central portion of the ingot which is likely to be uneven in the surface and the cross section of the aluminum alloy thick plate after the alumite treatment is obtained, so that it can be obtained and has an excellent appearance after the treatment of the aluminum oxide film. Aluminium alloy thick plate. It can also reduce the staggering situation in the batch. According to the first aspect of the invention, excellent surface condition, flatness, and thickness accuracy can be obtained. Further, by surface smoothing treatment, gas accumulation can be lost and high quality can be obtained. Further, since the surface appearance after the treatment of the aluminum oxide film hardly causes unevenness, it can be applied to various uses and can be recycled for other uses. [Embodiment] A method for producing an aluminum alloy thick plate and a thick alloy plate according to the present invention will be described in detail with reference to the drawings. Here, the invention of the present application will be described by dividing into (A) the first to fourth inventions, (B) the fifth to eighth inventions, (C) the ninth to twelfth inventions, and (D) the third invention. (A) Method for producing aluminum alloy thick plate according to the first to fourth aspects of the invention (1) Aluminium alloy thick plate according to the first to fourth inventions (hereinafter also referred to as "thickness -18-200900512 plate") The manufacturing method is as shown in Fig. 1, and the step (S1), the dehydrogenation step (S2), the filtration step (S3) (S 4 ), the cutting step (s 5 ), and the heat treatment step (s 6) are sequentially performed. ) Surface smoothing (S7) can be performed after the heat treatment step (s 6 ). In the present manufacturing method, first, the aluminum alloy thick plate (S 1 ) of the raw material is melted. Next, hydrogen gas is removed from the molten aluminum alloy in the hydrogen step (S2). Next, inclusions such as oxides and non-metals are removed by a filtration step. Next, the aluminum casting step (S4) is cast into an ingot. Then, the ingot is cut at (S 5 ) to form an aluminum alloy thick plate of a predetermined thickness. The aluminum alloy slab of a predetermined thickness is subjected to a heat treatment step (S6), and then, as needed, surface smoothing treatment is performed by a surface smoothing treatment step. (2) Ming alloy In the manufacturing method of the first to fourth inventions, a 5000-series Al-Mg alloy, a 3000-series gold, a 6000-series Al-Mg-Si alloy, and a 7000 alloy are used as raw materials. . The details are explained below. (2 -1) First invention A 5000-series Al-Mg alloy was used. The aluminum alloy contains % by mass to 12.0% by mass' and contains a mass selected from the group consisting of Si: 0.7: melting step and clock step. Further, if necessary, the processing step is in the melting step, by the step (S3), the alloy is in the cutting step, and then the hot portion (S7) is applied. The gold alloy, Al-Mn, A1 - Z η - M g

Mg： 1.5 %以下、 -19- 200900512Mg: 1.5% or less, -19-200900512

Fe: 0.8質量％以下、Cu: 0.6質量。/°以下、Μη·丨·0質里 %以下、Cr : 0.5質量％以下、Ζη : 〇·4質量％以下、Ti : 0.1質量％以下、Zr : 〇_3質量％以下中之至少1種’剩餘 部分爲A1及不可避免的雜質所構成。 以下說明各成分含量之數値限定的理由。 [M g : 1 . 5 質量 ％ ~ 1 2 質量 ％ ]Fe: 0.8% by mass or less and Cu: 0.6 mass. /° or less, Μη·丨·0 in the mass% or less, Cr: 0.5% by mass or less, Ζη: 〇·4 mass% or less, Ti: 0.1 mass% or less, and Zr: 〇_3 mass% or less. 'The remainder is made up of A1 and unavoidable impurities. The reason why the number of each component is limited is described below. [M g : 1.5 mass % ~ 1 2 mass % ]

Mg具有提昇鋁合金強度的效果。若Mg含量未達I5 質量％，前述效果低。另一方面’若Mg含量超過12質量 %，鑄造性顯著降低’無法進行製品的製造。因此’將M g 含量限定爲1 · 5質量％〜1 2質量％。 [S i : 0.7質量％以下]Mg has the effect of increasing the strength of the aluminum alloy. If the Mg content is less than I5 mass%, the aforementioned effect is low. On the other hand, if the Mg content exceeds 12% by mass, the castability is remarkably lowered. Therefore, the content of Mg is limited to 1.5% by mass to 12% by mass. [S i : 0.7% by mass or less]

Si具有提昇鋁合金強度的效果。Si，通常是以金屬材 料雜質的方式混入鋁合金中，在鑄造步驟（S4 )等，和 Mn、Fe —起在鑄塊中生成Al-(Fe)-(Mn)-Si系金屬間化合 物。若Si含量超過0.7質量％，會在鑄塊中生成粗大的金 屬間化合物，因此在氧化鋁膜處理後的表面外觀容易發生 不均勻。因此，將S i含量限定爲〇 _ 7質量％以下。 [F e : 0 · 8質量％以下] F e具有使鋁合金的結晶粒微細化、穩定化且提昇強度 的效果。Fe，通常是以金屬材料雜質的方式混入鋁合金 中’在鑄造步驟（S4)等’和Mn、Si —起在鑄塊中生成 -20- 200900512Si has the effect of increasing the strength of the aluminum alloy. Si is usually mixed into an aluminum alloy as a metal material impurity, and an Al-(Fe)-(Mn)-Si-based intermetallic compound is formed in the ingot together with Mn and Fe in the casting step (S4) or the like. If the Si content exceeds 0.7% by mass, a coarse intermetallic compound is formed in the ingot, so that the surface appearance after the treatment of the alumina film is likely to be uneven. Therefore, the Si content is limited to 〇 _ 7 mass% or less. [F e : 0 · 8 mass% or less] F e has an effect of refining and stabilizing the crystal grains of the aluminum alloy and improving the strength. Fe is usually mixed into an aluminum alloy by means of impurities in metallic materials. 'In the casting step (S4), etc., and Mn, Si are generated in the ingot -20- 200900512

Al-Fe-(Mn)-(Si)系金屬間化合物。若Fe含量超過0.8質量 %，會在鑄塊中生成粗大的金屬間化合物，因此在氧化鋁 膜處理後的表面外觀容易發生不均勻。因此，將Fe含量 限定爲0.8質量％以下。 [Cu : 0.6質量％以下]Al-Fe-(Mn)-(Si) intermetallic compound. If the Fe content exceeds 0.8% by mass, a coarse intermetallic compound is formed in the ingot, and thus the surface appearance after the treatment of the alumina film is likely to be uneven. Therefore, the Fe content is limited to 0.8% by mass or less. [Cu : 0.6% by mass or less]

Cu具有提昇鋁合金強度的效果。但爲了確保當作厚 板來使用的強度，Cu含量爲0.6質量％就足夠了。因此將 Cu含量限定爲0.6質量％以下。 [Mn : 1.0質量％以下] Μη的效果在於，藉由固熔於鋁合金中可提昇強度。 若Μη含量超過1.0質量％，會生成粗大的金屬間化合 物，因此在氧化鋁膜處理後的表面外觀容易發生不均勻。 因此，將Μη含量限定爲1 ·〇質量％以下。 [C r : 0.5質量％以下]Cu has the effect of increasing the strength of the aluminum alloy. However, in order to secure the strength to be used as a thick plate, a Cu content of 0.6% by mass is sufficient. Therefore, the Cu content is limited to 0.6% by mass or less. [Mn : 1.0% by mass or less] The effect of Μη is that the strength can be improved by solid-melting in an aluminum alloy. If the Μη content exceeds 1.0% by mass, a coarse intermetallic compound is formed, so that the surface appearance after the treatment of the alumina film is likely to be uneven. Therefore, the content of Μη is limited to 1% by mass or less. [C r : 0.5% by mass or less]

Cr的效果在於，在鑄造步驟（S4 )及熱處理步驟 (S6 )，會以微細化合物的方式析出而抑制結晶粒成長。 若Cr含量超過〇.5質量％，其初晶會形成粗大的Al-Cr系 金屬間化合物，因此在氧化鋁膜處理後的表面外觀容易發 生不均勻。因此，將C r含量限定爲0 · 5質量％以下。 [Zn : 0.4質量％以下] -21 - 200900512The effect of Cr is that in the casting step (S4) and the heat treatment step (S6), precipitation of fine crystals is suppressed to suppress crystal grain growth. When the Cr content exceeds 5% by mass, the primary crystal forms a coarse Al-Cr-based intermetallic compound, so that the surface appearance after the treatment of the aluminum oxide film tends to be uneven. Therefore, the C r content is limited to 0.5% by mass or less. [Zn: 0.4% by mass or less] -21 - 200900512

Zn具有提昇鋁合金強度的效果。但爲了確保當作厚 板來使用的強度，Zn含量爲0.4質量％就足夠了。因此將 Zn含量限定爲0.4質量％以下。 [Ti : 0· 1質量％以下]Zn has the effect of increasing the strength of the aluminum alloy. However, in order to secure the strength to be used as a thick plate, a Zn content of 0.4% by mass is sufficient. Therefore, the Zn content is limited to 0.4% by mass or less. [Ti : 0·1 mass% or less]

Ti具有讓鑄塊的結晶粒微細化之效果。若Ti含量超 過0.1質量％，前述效果達飽和。因此，將Ti含量限定爲 0.1質量％以下。 [Zr : 0.3質量％以下]Ti has an effect of making the crystal grains of the ingot fine. If the Ti content exceeds 0.1% by mass, the aforementioned effect is saturated. Therefore, the Ti content is limited to 0.1% by mass or less. [Zr : 0.3% by mass or less]

Zr具有讓鑄塊的結晶粒微細化的效果。若Zr含量超 過0.3質量％，前述效果達飽和。因此將Zr含量限定爲 0.3質量％以下。 [A1及不可避免的雜質：剩餘部分] A1合金，除前述成分以外，剩餘部分爲A1及不可避 免的雜質所構成。關於不可避免的雜質，例如包括V、B 等，該等雜質的含量各個只要在0.01質量％以下，就不會 影響本發明的鋁合金厚板的特性。 (2-2 )第2發明 使用3000系的Al-Mn合金。該銘合金，係含有Μη: 0.3質量％〜1.6質量％，且含有選自Si : 0.7質量％以下、 Fe : 0.8質量％以下、Cu : 0.5質量％以下、Mg : 1·5質量 -22- 200900512 %以下、C r : 0.3質量°/。以下、z n : 0.4質量％以下、 0 · 1質量％以下、Z r : 〇 . 3質量％以下中之至少1種’ 部分爲A1及不可避免的雜質所構成。 以下說明各成分的含量之數値限定的理由。 此外，關於Si、Fe、Cu、Cr、Zn、Ti及Zr之限 由以及不可避免的雜質，由於和前述A1-Mg系合金相 在此省略其說明。 [Μη : 0.3質量％〜1 · 6質量％] Μη的效果在於，藉由固溶於鋁合金中可提昇強 若Μη含量未達0.3質量％，前述效果低。若Μη含量 1 . 6質量％，會生成粗大的金屬間化合物，因此在氧 膜處理後的表面外觀容易發生不均勻。因此’將Μη 限定爲〇 · 3質量％〜1.6質量％。 [Mg : 1 .5質量。/。以下]Zr has an effect of making the crystal grains of the ingot fine. If the Zr content exceeds 0.3% by mass, the aforementioned effect is saturated. Therefore, the Zr content is limited to 0.3% by mass or less. [A1 and unavoidable impurities: the remaining portion] The A1 alloy is composed of A1 and unavoidable impurities in addition to the above components. The unavoidable impurities include, for example, V, B, etc., and the content of the impurities is not more than 0.01% by mass, and the characteristics of the aluminum alloy thick plate of the present invention are not affected. (2-2) Second invention A 3000-series Al-Mn alloy was used. The alloy contains Μη: 0.3% by mass to 1.6% by mass, and is selected from the group consisting of Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.5% by mass or less, and Mg: 1.9 mass% - 22 200900512% below, C r : 0.3 mass ° /. Hereinafter, z n : 0.4% by mass or less, 0 · 1% by mass or less, and Z r : 〇. At least one of the 3% by mass or less is composed of A1 and unavoidable impurities. The reason why the content of each component is limited will be described below. Further, the limits of Si, Fe, Cu, Cr, Zn, Ti, and Zr and the unavoidable impurities are omitted from the above-mentioned A1-Mg-based alloy phase. [Μη : 0.3 mass% to 1 · 6 mass%] The effect of Μη is that the solid solution of the aluminum alloy can increase the strength of the Μη content to less than 0.3% by mass, and the aforementioned effect is low. If the Μη content is 1.6% by mass, a coarse intermetallic compound is formed, so that the surface appearance after the oxygen film treatment tends to be uneven. Therefore, Μη is limited to 〇·3 mass% to 1.6 mass%. [Mg: 1.5 quality. /. the following]

Mg具有提昇鋁合金強度的效果。但爲了確保當 板來使用的強度，Mg含量爲1_5質量％就足夠了。因 Mg含量限定爲1.5質量％以下。 (2-3 )第3發明 使用6000系的Al-Mg-Si系合金。該銘合金’係 S i : 0 · 2質量％〜1 . 6質量％、M g : 0 · 3質量％〜1 _ 5 %，且含有選自Fe : 〇.8質量％以下、Cu ·· 1 ·0質量Mg has the effect of increasing the strength of the aluminum alloy. However, in order to ensure the strength of the use of the sheet, a Mg content of 1 - 5 mass% is sufficient. The Mg content is limited to 1.5% by mass or less. (2-3) Third invention A 6000-based Al-Mg-Si alloy is used. The alloy "S i : 0 · 2 mass % ~ 1. 6 mass %, M g : 0 · 3 mass % ~ 1 _ 5 %, and contains Fe: 〇. 8 mass% or less, Cu ·· 1 · 0 quality

Ti ： 剩餘 定理 同， 度。 超過 化鋁 含量 作厚 此將 含有 質量 %以 -23- 200900512 下、Μ η : 0.6質量％以下、c r : 0 · 5質量％以下、Ζ η : 0.4 質量％以下、Ti : 〇. 1質量％以下、zr : 0·3質量％以下中之 至少1種’剩餘部分爲Α1及不可避免的雜質所構成。 以下說明各成分的含量之數値限定的理由。 此外，關於Fe、Mn、Cr、Ti及Zr之限定理由以及不 可避免的雜質’由於和前述A Ι-Mg系合金相同，在此省略 其說明。 [S i : 〇 · 2質量％〜1 · 6質量0/〇 ]Ti : Remainder Theorem Same, degree. When the content exceeds the aluminum content, the mass% is -23-200900512, Μ η : 0.6 mass% or less, cr: 0 · 5 mass% or less, Ζ η : 0.4 mass% or less, Ti: 〇. 1 mass% Hereinafter, at least one of zr: 0·3 mass% or less 'the remaining portion is Α1 and an unavoidable impurity. The reason why the content of each component is limited will be described below. Further, the reason for limiting the Fe, Mn, Cr, Ti, and Zr and the unavoidable impurities ' are the same as those of the above A Ι-Mg-based alloy, and the description thereof is omitted here. [S i : 〇 · 2% by mass to 1 · 6 masses 0/〇 ]

Si具有提昇鋁合金強度的效果。Si，通常是以金屬材 料雜質的方式混入鋁合金中，在鑄造步驟（S4)等，在鑄 塊中生成Al-(Fe)-Si系金屬間化合物及Si系金屬間化合 物。若s i含量未達0.2質量％，前述效果低。若S i含量 超過1.6質量％，會在鑄塊中生成粗大的S i系金屬間化合 物，因此在氧化鋁膜處理後的表面外觀容易發生不均勻。 因此，將Si含量限定爲0.2質量％〜I·6質量％。 [M g : 0.3質量％〜1 . 5質量％ ]Si has the effect of increasing the strength of the aluminum alloy. Si is usually mixed into an aluminum alloy as a metal material impurity, and an Al-(Fe)-Si-based intermetallic compound and a Si-based intermetallic compound are formed in the ingot in the casting step (S4). If the s i content is less than 0.2% by mass, the aforementioned effect is low. When the Si content exceeds 1.6% by mass, a coarse Si-based intermetallic compound is formed in the ingot, and thus the surface appearance after the treatment of the alumina film is likely to be uneven. Therefore, the Si content is limited to 0.2% by mass to 1.6% by mass. [M g : 0.3% by mass to 1. 5 mass%]

Mg的效果在於，藉由和Si共存來形成Mg2Si以提昇 鋁合金的強度。若Mg含量未達〇.3質量％，前述效果 低。若Mg含量超過1.5質量％ ’前述效果達飽和。因此 將M g含量限定爲0 · 3質量％〜1 · 5質量％。 [Cu : 1.0質量％以下] -24- 200900512The effect of Mg is to form Mg2Si by coexistence with Si to enhance the strength of the aluminum alloy. If the Mg content is less than 3% by mass, the aforementioned effect is low. If the Mg content exceeds 1.5% by mass, the aforementioned effect is saturated. Therefore, the Mg content is limited to 0. 3 mass% to 1 · 5 mass%. [Cu : 1.0% by mass or less] -24- 200900512

Cu具有提昇鋁合金強度的效果。若Cu含量超過 質量％ ’其耐蝕性變差。因此將Cu含量限定爲1 ·〇質量％ 以下。 [Zn : 0.4質量％以下]Cu has the effect of increasing the strength of the aluminum alloy. If the Cu content exceeds the mass %', the corrosion resistance is deteriorated. Therefore, the Cu content is limited to 1% by mass or less. [Zn : 0.4% by mass or less]

Zn具有提昇鋁合金強度的效果。若Zn含量超過0‘4 質量％ ’其耐蝕性變差。因此將Zn含量限定爲0.4質量°/。 以下。 (2 - 4 )第4發明 使用70 00系的Al-Zn-Mg系合金。該鋁合金’係含有 Mg: 〇_4質量％〜4.0質量％、Zn: 3.0質量％〜9.0質量 % ’且含有選自s i : 0.7質量。/。以下、F e : 0 · 8質量％以 下、Cu : 3_0質量％以下、Μη : 0.8質量％以下、Cr : 0.5 質量％以下、Ti : 〇· 1質量％以下、Zr : 0·25質量％以下中 之至少1種，剩餘部分爲Α1及不可避免的雜質所構成。 以下說明各成分的含量之數値限定的理由。 此外，關於Cr、Ti及Zr之限定理由以及不可避免的 #質’由於和前述A1-Mg系合金相同，在此省略其說明。 [Mg : 0_4質量％〜4.0質量％]Zn has the effect of increasing the strength of the aluminum alloy. If the Zn content exceeds 0 '4% by mass', the corrosion resistance deteriorates. Therefore, the Zn content is limited to 0.4 mass%/. the following. (2 - 4) The fourth invention uses a 70-00-series Al-Zn-Mg-based alloy. The aluminum alloy ' contains Mg: 〇 4% by mass to 4.0% by mass, Zn: 3.0% by mass to 9.0% by mass', and contains s i : 0.7 mass. /. Hereinafter, F e : 0 · 8 mass% or less, Cu: 3_0 mass% or less, Μη: 0.8 mass% or less, Cr: 0.5 mass% or less, Ti: 〇·1 mass% or less, and Zr: 0·25 mass% or less At least one of them, the remainder being composed of Α1 and unavoidable impurities. The reason why the content of each component is limited will be described below. In addition, the reason for the limitation of Cr, Ti, and Zr and the unavoidable #质' are the same as those of the above-described A1-Mg-based alloy, and the description thereof is omitted here. [Mg : 0_4% by mass to 4.0% by mass]

Mg具有提昇鋁合金強度的效果。若Mg含量未達0.4 質量％，前述效果低。另一方面，若Mg含量超過4.0質 4 % ’氧化鋁膜處理後的表面外觀容易發生不均勻。因此 -25- 200900512 將Mg含量限定爲0·4質量％〜4.0質量％。 [Ζη : 3.0質量％〜9.0質量％ ] Ζη具有提昇鋁合金強度的效果。若Ζη含量未達3.0 質量％，前述效果低。另一方面，若Ζη含量超過9.0質量 %，氧化鋁膜處理後的表面外觀容易發生不均勻。因此將 Ζη含量限定爲3.0質量％〜9.0質量％。 [Si : 0.7質量％以下]Mg has the effect of increasing the strength of the aluminum alloy. If the Mg content is less than 0.4% by mass, the aforementioned effect is low. On the other hand, if the Mg content exceeds 4.0 mass%, the surface appearance after the treatment with the aluminum oxide film tends to be uneven. Therefore, -25-200900512 limits the Mg content to 0.4% by mass to 4.0% by mass. [Ζη : 3.0% by mass to 9.0% by mass] Ζη has an effect of improving the strength of the aluminum alloy. If the Ζη content is less than 3.0% by mass, the aforementioned effect is low. On the other hand, if the Ζη content exceeds 9.0% by mass, the surface appearance after the treatment of the aluminum oxide film tends to be uneven. Therefore, the content of Ζη is limited to 3.0% by mass to 9.0% by mass. [Si : 0.7% by mass or less]

Si’通常是以金屬材料雜質的方式混入鋁合金中，在 鑄造步驟（S4 )等，在鑄塊中生成Al-(Fe)_Si系金屬間化 合物。若Si含量超過0.7質量％，會在鑄塊中生成粗大的 Al-(Fe)-Si系金屬間化合物，因此在氧化鋁膜處理後的表 面外觀容易發生不均勻。因此，將Si含量限定爲0.7質量 %以下。 [Fe : 0.8質量％以下]Si' is usually mixed into the aluminum alloy as a metal material impurity, and an Al-(Fe)_Si-based intermetallic compound is formed in the ingot in the casting step (S4) or the like. When the Si content exceeds 0.7% by mass, a coarse Al-(Fe)-Si-based intermetallic compound is formed in the ingot, and thus the surface appearance after the treatment of the alumina film is likely to be uneven. Therefore, the Si content is limited to 0.7% by mass or less. [Fe : 0.8% by mass or less]

Fe，通常是以金屬材料雜質的方式混入鋁合金中，在 鑄造步驟（S4 )等，在鑄塊中生成Al-Fe系金屬間化合 物。若Fe含量超過0.8質量％，會在鑄塊中生成粗大的 Al-Fe系金屬間化合物’因此在氧化鋁膜處理後的表面外 觀容易發生不均勻。因此’將Fe含量限定爲0.8質量％以 下。 -26- 200900512 [Cu : 3.0質量％以下]Fe is usually mixed into the aluminum alloy as a metal material impurity, and an Al-Fe-based intermetallic compound is formed in the ingot in the casting step (S4) or the like. When the Fe content exceeds 0.8% by mass, a coarse Al-Fe-based intermetallic compound is formed in the ingot. Therefore, unevenness is likely to occur on the surface appearance after the treatment of the alumina film. Therefore, the Fe content is limited to 0.8% by mass or less. -26- 200900512 [Cu : 3.0% by mass or less]

Cu具有提昇鋁合金強度的效果。若Cu含量超過3.0 質量％，其耐蝕性變差。因此將Cu含量限定爲3.0質量％ 以下。 [Μη : 0.8質量％以下] Μη具有讓結晶組織微細化的效果。若Μη含量超過 0.8質量％，會生成粗大的金屬間化合物，因此在氧化鋁 膜處理後的表面外觀容易發生不均勻。因此，將Μη含量 限定爲0.8質量％以下。 (3 )製造方法的詳細內容 接著說明第1至第4發明之製造方法之各步驟。 (3 _ 1 )熔解步驟 熔解步驟（S 1 )，是將原料之鋁合金熔解的步驟。 (3-2 )脫氫氣步驟 脫氫氣步驟（S2 )，係從在熔解步驟（s 1 )熔解後的 金呂合金除去氣氣的步驟。 氫氣，是從燃料中的氫、附著於金屬材料之水分及有 機物等所產生。若含有多量的氫氣，會發生下述問題。 [a] 發生針孔。 [b] 製品強度變差。 -27- 200900512 [C]在鑄塊表面附近的粒界，發生氫之集積、 此，會發生鑄塊的鼓起，以及起因於鼓起之鋁合 捲起。又會發生，可形成厚板的表面缺陷之厚板 在缺陷。 因此，在鋁合金100g中，氫氣含量宜爲 下’更佳爲0.1ml以下。爲了除去氫氣，可對熔 熔劑處理、氯精煉、線上精煉等，又更佳爲，進 氫氣裝置中使用吸氣裝置（snifter)或多孔塞 plug)(參照日本特開2002- 1 4644號公報）。 鑄塊之氫氣濃度，例如能用以下方式來求出 從鑄造步驟後的鑄塊切割出樣本。接著，用乙醇 樣本施以超音波洗淨。然後，用例如非活性氣體 熱傳導度法（LIS A06-1993)來處理該樣本。 鋁合金厚板的氫氣濃度，例如能用以下方式 亦即，從銘合金厚板切割出樣本。接著，將樣 NaOΗ水溶液。然後用硝酸處理來除去樣本表面 膜。然後，用乙醇和丙酮將樣本施以超音波洗淨 例如用真空加熱抽出容量法（LIS Α06_1993) 本。 (3-3 )過濾步驟 過濾步驟（S 3 )，是藉由過濾裝置從鋁合金 物（主要爲氧化物和非金屬）的步驟。在過濾裝 設置陶瓷管（使用1mm左右的粒子之氧化鋁） 濃化。因 金厚板的 表面的潛 0 2 m 1 以 融液進行 一步在脫 (porous 。亦即， 和丙酮將 氣流熔解 來求出。 本浸漬於 的氧化皮 。接著， 來處理樣 除去夾雜 置，例如 。藉由使 -28- 200900512 熔融液通過前述陶瓷管來除去前述夾雜物。 經由前述脫氫氣步驟及過濾步驟，在接下來的鑄造步 驟（S 4 )，可從確保高品質之鋁合金獲得鑄塊。由於可抑 制氧化物的堆積物（浮渣）之生成，故能減少除去浮渣的 作業。 (3-4)鑄造步驟 鑄造步驟（S4 )，是將鋁合金熔融液成形固化成長方 體形等既定形狀，以製造出鑄塊。例如，使用具備水冷鑄 模之鑄造裝置。鑄造方法是採用半連續鑄造法。在半連續 鑄造法，是對底部打開之金屬製水冷鑄模，從上方注入鋁 合金的熔融液，並從水冷鑄模的底部將凝固後的鋁合金連 續取出。藉此獲得既定厚度的鑄塊。又半連續鑄造法，能 採用縱向或橫向的方式來進行。 (3-5 )切割步驟 切割步驟（S 5 )，係將鑄造步驟（S4 )製得的鑄塊切 割成既定厚度的鋁合金厚板之步驟。關於切割方法，可採 用厚板（slab )切割法。在厚板切割法，是將前述半連續 鑄造法所製得之鑄塊，用帶鋸切斷機等沿鑄造方向進行切 割，以獲得既定厚度的鋁合金厚板。鋁合金厚板較佳爲1 5 〜2 00mm，但沒有特別的限定，可依厚板的用途來適當調 整。 作爲切割方法，雖以使用帶鋸爲佳，但沒有特別的限 29- 200900512 定’也能使用圓鋸切斷機、雷射 '水壓等等。 比起壓延的情形’若將鑄塊施以切割，可獲得表面狀 態、平坦度及板厚精度等優異之鋁合金厚板。例如可獲 得：平坦度（彎曲量）爲0.4mm以下/鑄造方向im長，且 板厚精度爲±l〇〇"m以下之鋁合金厚板。 又如第2圖所示，在切割步驟（S 5 )，較佳爲將斜線 之中央部分B除去。該中央部分B，是從厚度方向中央a 朝厚度方向之各表面具有均等的厚度，且設鑄塊1厚度爲 丁的情形’合計具有T/30〜T/5的厚度。在第2圖，中央 部分B具有約T/5的厚度。在此，鑄塊1之中央部分B之 上下厚度b 1、b 2，雖以相同爲佳，但容許3 0 %程度的差 異。前述厚度方向中央A是指，鑄塊1之厚度方向中央， 且鑄塊1的厚度T的約1/2、亦即約T/2的部位。 在鑄塊1的中央部分B，在氧化鋁膜處理後之厚板表 面及截面容易發生不均勻。在切割步驟（S5)，藉由將該 中央部分B除去，可獲得氧化鋁膜處理後之外觀優異的厚 板。又能減少批次內的參差情形。另一方面，若除去的厚 度未達173 0，容易發生在氧化鋁膜處理後的表面外觀具有 不均勻的厚板，且批次內的參差情形容易發生。另一方 面，若除去的厚度超過T/5，除去量變得過多，可能造成 生產性變差。因此，鑄塊1之中央部分B的除去量較佳爲 限定成，從厚度方向中央A朝厚度方向之各表面具有均等 的厚度，且設鑄塊1厚度爲T的情形，合計具有T/30〜 T/5的厚度。 -30- 200900512 在經由前述切割步驟（s5 )將鑄塊切割後，在接下來 的熱處理步驟（S 6 )，爲了謀求內部應力的除去及內部組 織的均一化而實施熱處理。藉由實施熱處理，可提昇平坦 度、板厚精度以及氧化鋁膜處理後的外觀特性。 (3-6)熱處理步驟 熱處理步驟（S6 )，係將切割步驟（S 5 )所得之既定 厚度的鋁合金厚板實施熱處理（均質化熱處理）的步驟。 熱處理可依通常方法來實施。亦即，在鋁合金爲5000系 的Al-Mg系合金（第1發明）、3000系的Al-Mn合金 (第2發明）、6000系的Al-Mg-Si系合金（第3發明） 的情形，是藉由在400°C以上未達熔點的溫度保持1小時 以上來進行熱處理。又在鋁合金是7000系的Al-Zn-Mg系 合金（第4發明）的情形，是藉由在3 5 0 °C以上未達熔點 之溫度保持1小時以上來進行熱處理。 若將鑄造步驟（S 4 )所製得之鑄塊實施切割加工，由 於內部殘留應力會釋放出，而容易發生彎曲。然而，在本 發明’由於將切割加工後的既定厚度之鋁合金厚板，例如 放在定盤等上來實施熱處理，因此可提昇平坦度。 在第1至第3發明中，若處理溫度未達400。(：，內部 應力的除去量少，在鑄造中偏析的熔質元素之均質化不 足，因此熱處理的效果低。於是將處理溫度限定爲400r 以上。又若處理溫度在熔點以上，在內部會發生局部熔融 而產生內部缺陷’又強度和延展性會變差。因此將處理溫 -31 - 200900512 度限定爲未達熔點。 在第4發明，若處理溫度未達350 °C，內部應力的除 去量少，在鑄造中偏析的熔質元素之均質化不足，因此熱 處理的效果低。於是將處理溫度限定爲3 5 0 °C以上。又若 處理溫度在熔點以上，在內部會發生局部熔融而產生內部 缺陷，又強度和延展性會變差。因此將處理溫度限定爲未 達熔點。 若處理時間未達1小時，金屬間化合物之固熔程度不 夠’容易析出金屬間化合物。因此，將處理時間限定爲1 小時以上。又若處理時間超過8小時，熱處理的效果達飽 和，將造成能量損耗。因此宜將處理時間限定爲8小時以 內。 在前述熱處理步驟（S 6 )熱處理後的鋁合金厚板，爲 了除去形成於厚板表面之晶出物和氧化物，或爲了抑制厚 板表面之氣體堆積，視需要可實施表面平滑化處理。 (3 - 7 )表面平滑化處理步驟 表面平滑化處理步驟（S 7 )，是對熱處理步驟（S 6 ) 所製得之鋁合金厚板的表面，實施表面平滑化處理的步 驟。作爲表面平滑化處理法，可採用：端銑切削、鑽石車 刀切削等的切削法；將表面用磨石等磨削之磨削法；拋光 硏磨等的硏磨法等等；但不限於此。 將鋁合金厚板應用於真空裝置用室的情形，實施表面 平滑化處理特別有效。其理由如下所說明。亦即，真空裝 -32- 200900512 置用室減壓至高真空的情形，起因於從室內側表面放 吸附氣體，或是起因於固熔於厚板中的氣體原子朝表 出，會造成真空度變差。因此，到達目標真空度的時 長，生產效率變差。基於此，應用於該室之鋁合金厚 須要求：吸附於厚板（位於室內側）表面之氣體少， 形成高真空仍不會放出固熔於厚板中的氣體原子。 (B)第5至第8發明之鋁合金厚板之製造方法 (1 )製造方法之槪要 第5至第8發明之鋁合金厚板之製造方法，如第 所示，係依序進行：熔解步驟（S1 )、脫氫氣 (S2 )、過濾步驟（S3 )、鑄造步驟（S4 )、熱處理 (S5 )、切割步驟（S6 )。又視需要，可在切割 (S 6 )後進行表面平滑化處理步驟（S 7 )。 在本製造方法，首先，將原料之鋁合金厚板在熔 驟（S 1 )進行熔解。接著，從熔解後的鋁合金中，藉 氫氣步驟（S2)來除去氫氣。接著，藉由過濾步驟（ 來除去氧化物和非金屬等的夾雜物。接著，該鋁合金 鑄造步驟（S4 )鑄造成鑄塊。然後，該鑄塊在熱處理 (S 5 )進行熱處理後，在切割步驟（S 5 )進行切割而 既定厚度的鋁合金厚板。接著，對於既定厚度的鋁合 板’按照需要’藉由表面平滑化處理步驟（S 7 )來進 面平滑化處理。 出之 面放 間變 板必 即使 3圖 步驟 步驟 步驟 解步 由脫 S3 ) 是在 步驟 形成 金厚 行表 -33- 200900512 (2 )錯合金 在第5至第8發明之製造方法，作爲原料之鋁合金， 係分別使用5 000系之Ai_Mg合金，3 000系之Al-Mn合 金’ 6000系之Al-Mg-Si系合金以及7000系之Al-Zn-Mg 合金。具體內容說明如下。 (2-1 )第5發明 使用和第1發明相同的5000系之Al-Mg合金。該鋁 合金之組成、成分含量、含量之數値限定的理由，都和第 1發明相同。 (2-2 )第6發明 使用和第2發明相同的3 000系之Al-Mn合金。該鋁 合金之組成、成分含量、含量之數値限定的理由，都和第 2發明相同。 (2-3 )第7發明 使用和第3發明相同的6000系之Al-Mg-Si系合金。 該鋁合金之組成、成分含量、含量之數値限定的理由，都 和第3發明相同。 (2-4 )第8發明 使用和第4發明相同的7000系之Al-Zn-Mg合金。該 鋁合金之組成、成分含量、含量之數値限定的理由’都和 -34- 200900512 第4發明相同。 (3 )製造方法的詳細 接著詳細說明第5至第8發明之製造方法之各步驟。 (3 -1 )熔解步驟 是和第1至第4發明之熔解步驟（si)相同。 (3-2 )脫氫氣步驟 是和第1至第4發明之脫氫氣步驟（S2)相同。 (3 - 3 )過濾步驟 是和第1至第4發明之過濾步驟（S3)相同。 (3-4 )鑄造步驟 是和第1至第4發明之鑄造步驟（S4)相同。 在將鑄造步驟（S4 )所製得的鑄塊施以切割後’在接 下來的熱處理步驟（S 5 )，基於除去內部應力及讓內部組 織均一化的目的，實施熱處理。藉由對前述鑄塊實施熱處 理，可提昇平坦度、板厚精度、氧化鋁膜處理後的外觀性 狀。 (3 - 5 )熱處理步驟 熱處理步驟（S5 )，是將鑄造步驟（S4 )所製得的_ -35- 200900512 塊實施熱處理（均質化熱處理）的步驟。熱處理可依通常 方法來實施。亦即，在鋁合金爲5 000系的A1-Mg系合金 (第5發明）、3000系的Al-Mn合金（第6發明）、 6000系的Al-Mg-Si系合金（第7發明）的情形，是藉由 在200°C以上未達400°C的溫度保持1小時以上來進行熱 處理。又在鋁合金是7000系的Al-Zn-Mg系合金（第8發 明）的情形，是藉由在2 0 0 °C以上未達3 0 0 °C之溫度保持1 小時以上來進行熱處理。 在第5至第7發明，若處理溫度未達200 °C，內部應 力的除去量少，實施熱處理之效果低。因此將處理溫度限 定爲2 0 0 °C以上。又若處理溫度爲4 0 0 °C以上，延展性變 高，強度和切削性變差。切削性代表切屑斷裂性。切屑以 斷裂成細小爲佳。其原因在於，若切屑長，會纏在加工工 具（刀）上而一起旋轉，如此會造成厚板表面受傷、工具 破損。因此將處理溫度限定爲未達400 °C。藉由以這種溫 度條件來進行熱處理，不致降低強度和切削性，且能提昇 平坦度及板厚精度。 在第8發明，若處理溫度未達200 °C，內部應力的除 去量少，實施熱處理之效果低。因此將處理溫度限定爲 2 00°C以上。又若處理溫度爲3 5 0 °C以上，延展性變高，強 度和切削性變差。切削性代表切屑斷裂性。切屑以斷裂成 細小爲佳。其原因在於，若切屑長，會纏在加工工具 (刀）上而一起旋轉，如此會造成厚板表面受傷、工具破 損。因此將處理溫度限定爲未達3 5 0 °C。藉由以這種溫度 -36- 200900512 條件來進行熱處理，不致降低強度和切削性，且能提昇平 坦度及板厚精度。 若處理時間未達1小時，金屬間化合物之固熔程度不 夠，容易析出金屬間化合物。因此’將處理時間限定爲1 小時以上。又若處理時間超過8小時’熱處理的效果達飽 和，將造成能量損耗。因此宜將處理時間限定爲8小時以 內。 (3-6 )切割步驟 切割步驟（S 6 )是將熱處理步驟（S 5 )所得的鑄塊切 割成既定厚度的鋁合金厚板的步驟。其詳細內容和第1至 第4發明之切割步驟（S 5 )相同。 在前述切割步驟（S 6 )後的鋁合金厚板，爲了除去形 成於厚板表面之晶出物和氧化物，或爲了抑制厚板表面之 氣體堆積，視需要可實施表面平滑化處理。 (3-7 )表面平滑化處理步驟 表面平滑化處理步驟（S 7 )，是對切割步驟（S 6 )所 得之銘合金厚板的表面實施表面平滑化處理的步驟。其詳 細內容和第1至第4發明之表面平滑化處理步驟（S 7 )相 同。 (C)第9至第12發明之鋁合金厚板之製造方法 (1 )製造方法的槪要 -37- 200900512 第9至第12發明之鋁合金厚板（以下也稱爲「厚 板」）之製造方法，如第1圖所示，係依序進行：熔解步 驟（S1)、脫氫氣步驟（S2)、過濾步驟（S3)、鑄造步 驟（S4)、切割步驟（S5)、熱處理步驟（S6)。又視需 要’可在熱處理步驟（S6)後進行表面平滑化處理步驟 (S7 ) 〇 在本製造方法，首先，將原料之鋁合金厚板在熔解步 驟（S 1 )進行熔解。接著，從熔解後的鋁合金中，藉由脫 氫氣步驟（S2)來除去氫氣。接著，藉由過濾步驟（S3) 來除去氧化物和非金屬等的夾雜物。接著，該鋁合金是在 鑄造步驟（S4 )鑄造成鑄塊。然後，該鑄塊在切割步驟 (S 5 )進行切割而形成既定厚度的鋁合金厚板。然後，將 既定厚度的鋁合金厚板藉由熱處理步驟（S6)進行熱處 埋，接著，按照需要，藉由表面平滑化處理步驟（S7)來 進行表面平滑化處理。 (2)鋁合金 在第9至第12發明之製造方法’作爲原料之鋁合 金’係分別使用5000系之Al-Mg合金，3000系之Al-Mn 合金，6000系之Al-Mg-Si系合金以及7000系之Al-Zn-Cu has the effect of increasing the strength of the aluminum alloy. If the Cu content exceeds 3.0% by mass, the corrosion resistance is deteriorated. Therefore, the Cu content is limited to 3.0% by mass or less. [Μη : 0.8% by mass or less] Μη has an effect of making the crystal structure fine. If the Μη content exceeds 0.8% by mass, a coarse intermetallic compound is formed, so that the surface appearance after the treatment of the alumina film is likely to be uneven. Therefore, the Μη content is limited to 0.8% by mass or less. (3) Details of Manufacturing Method Next, each step of the manufacturing method of the first to fourth inventions will be described. (3 _ 1) Melting step The melting step (S 1 ) is a step of melting the aluminum alloy of the raw material. (3-2) Dehydrogenation step The dehydrogenation step (S2) is a step of removing the gas from the gold alloy after the melting step (s 1 ) is melted. Hydrogen is produced from hydrogen in fuel, moisture attached to metal materials, and organic matter. If a large amount of hydrogen is contained, the following problems occur. [a] A pinhole has occurred. [b] The strength of the product deteriorates. -27- 200900512 [C] At the grain boundary near the surface of the ingot, hydrogen accumulation occurs, and the bulging of the ingot and the aluminum coil caused by the bulging occur. It will happen again, and the thick plate that can form the surface defects of the thick plate is defective. Therefore, in 100 g of the aluminum alloy, the hydrogen content is preferably lower than 0.1 ml. In order to remove hydrogen, it is possible to use a fluxing device, a chlorine refining, an in-line refining, etc., and it is more preferable to use a suction device or a porous plug in a hydrogen inlet device (refer to Japanese Laid-Open Patent Publication No. 2002-1-4644). . The hydrogen concentration of the ingot can be determined, for example, by cutting the sample from the ingot after the casting step. Next, the ethanol sample was subjected to ultrasonic cleaning. The sample is then treated with, for example, an inert gas thermal conductivity method (LIS A06-1993). The hydrogen concentration of the aluminum alloy thick plate can be, for example, cut out from the alloy plate by the following method. Next, a sample of NaO hydrazine was added. The nitric acid treatment is then used to remove the sample surface film. Then, the sample is subjected to ultrasonic cleaning with ethanol and acetone, for example, by vacuum heating extraction capacity method (LIS Α 06_1993). (3-3) Filtration Step The filtration step (S 3 ) is a step of removing the aluminum alloy (mainly oxide and non-metal) by a filtering device. The ceramic tube (aluminum using a particle of about 1 mm) was concentrated in a filter. The potential of the surface of the gold plate is 0 2 m 1 and is melted in one step (porous, that is, the air flow is melted with acetone to obtain the oxide scale which is immersed. Then, the sample is removed to remove the inclusions. For example, the inclusions are removed by passing the -28-200900512 melt through the ceramic tube. Through the aforementioned dehydrogenation step and filtration step, in the next casting step (S 4 ), it can be obtained from a high quality aluminum alloy. Since the ingot can suppress the formation of oxide deposits (scum), the operation of removing the dross can be reduced. (3-4) Casting step The casting step (S4) is to form and solidify the aluminum alloy melt. A shape such as a body shape to produce an ingot. For example, a casting device having a water-cooled mold is used. The casting method is a semi-continuous casting method. In the semi-continuous casting method, a metal water-cooling mold is opened to the bottom, and aluminum is injected from above. a molten alloy of the alloy, and continuously extracting the solidified aluminum alloy from the bottom of the water-cooled mold, thereby obtaining an ingot of a predetermined thickness, and a semi-continuous casting method capable of adopting a longitudinal (3-5) Cutting step The cutting step (S 5 ) is a step of cutting the ingot obtained by the casting step (S4) into an aluminum alloy thick plate of a predetermined thickness. The slab cutting method is adopted. In the thick plate cutting method, the ingot obtained by the above-described semi-continuous casting method is cut in a casting direction by a band saw cutter to obtain a thick aluminum alloy of a predetermined thickness. The aluminum alloy thick plate is preferably from 1 5 to 2 00 mm, but is not particularly limited and can be appropriately adjusted according to the use of the thick plate. As the cutting method, it is preferable to use a band saw, but there is no special limit 29- 200900512 can also use circular saw cutting machine, laser 'water pressure, etc.. Compared with the case of rolling', if the ingot is cut, the aluminum alloy with excellent surface condition, flatness and thickness accuracy can be obtained. For example, it is possible to obtain an aluminum alloy thick plate having a flatness (bending amount) of 0.4 mm or less/long casting direction and a thickness accuracy of ±1 〇〇"m. In the cutting step (S 5 ), preferably the central portion B of the oblique line The central portion B has a uniform thickness from the center a in the thickness direction toward each surface in the thickness direction, and the case where the thickness of the ingot 1 is diced 'total has a thickness of T/30 to T/5. The central portion B has a thickness of about T/5. Here, the lower thicknesses b 1 and b 2 of the central portion B of the ingot 1 are preferably the same, but allow a difference of about 30%. The center A is a portion in the thickness direction of the ingot 1 and a thickness T of the ingot 1 of about 1/2, that is, a portion of about T/2. In the central portion B of the ingot 1, after the alumite treatment The surface and the cross section of the thick plate are likely to be uneven. In the cutting step (S5), by removing the central portion B, a thick plate excellent in appearance after the treatment of the aluminum oxide film can be obtained. It can also reduce the staggering situation in the batch. On the other hand, if the thickness to be removed is less than 173, it tends to have uneven slabs on the surface after the treatment of the alumina film, and the unevenness in the batch is likely to occur. On the other hand, if the removed thickness exceeds T/5, the amount of removal becomes excessive, which may cause deterioration in productivity. Therefore, the removal amount of the central portion B of the ingot 1 is preferably limited to have a uniform thickness from the center A in the thickness direction toward the thickness direction, and the thickness of the ingot 1 is T, and the total has T/30. ~ T/5 thickness. -30- 200900512 After the ingot is cut through the above-described cutting step (s5), heat treatment is performed in the subsequent heat treatment step (S6) in order to remove internal stress and homogenize the internal structure. By performing heat treatment, the flatness, the thickness accuracy, and the appearance characteristics after the treatment of the aluminum oxide film can be improved. (3-6) Heat treatment step The heat treatment step (S6) is a step of subjecting the aluminum alloy thick plate of a predetermined thickness obtained by the cutting step (S 5 ) to heat treatment (homogenization heat treatment). The heat treatment can be carried out in accordance with a usual method. In other words, the aluminum alloy is a 5000-series Al-Mg-based alloy (first invention), a 3000-series Al-Mn alloy (second invention), and a 6000-series Al-Mg-Si alloy (third invention). In this case, the heat treatment is carried out by maintaining the temperature at 400 ° C or higher and not reaching the melting point for 1 hour or more. Further, in the case where the aluminum alloy is a 7000-series Al-Zn-Mg-based alloy (the fourth invention), the heat treatment is carried out by maintaining the temperature at 350 ° C or higher for less than 1 hour. If the ingot obtained by the casting step (S 4 ) is subjected to a cutting process, the internal residual stress is released and the bending is liable to occur. However, in the present invention, since the heat treatment is performed by placing the aluminum alloy thick plate of a predetermined thickness after the cutting process, for example, on a fixed plate or the like, the flatness can be improved. In the first to third inventions, the processing temperature is less than 400. (: The amount of removal of internal stress is small, and the homogenization of the molten element segregated during casting is insufficient, so the effect of heat treatment is low. Therefore, the treatment temperature is limited to 400 r or more. If the treatment temperature is above the melting point, it occurs internally. Local melting and internal defects will deteriorate the strength and ductility. Therefore, the treatment temperature -31 - 200900512 is limited to the non-melting point. In the fourth invention, if the treatment temperature is less than 350 °C, the internal stress is removed. Since the homogenization of the molten element segregated during casting is insufficient, the effect of the heat treatment is low. Therefore, the treatment temperature is limited to 350 ° C or higher. If the treatment temperature is above the melting point, local melting occurs inside. Internal defects, strength and ductility will be worse. Therefore, the treatment temperature is limited to less than the melting point. If the treatment time is less than 1 hour, the degree of solid solution of the intermetallic compound is not enough 'easy to precipitate intermetallic compounds. Therefore, the treatment time will be It is limited to more than 1 hour. If the treatment time exceeds 8 hours, the effect of heat treatment is saturated, which will cause energy loss. The time is limited to 8 hours. The aluminum alloy thick plate after the heat treatment step (S 6 ) is heat treated, in order to remove crystals and oxides formed on the surface of the thick plate, or to suppress gas accumulation on the surface of the thick plate, as needed Surface smoothing treatment can be carried out. (3 - 7) Surface smoothing treatment step The surface smoothing treatment step (S7) is to perform surface smoothing on the surface of the aluminum alloy thick plate obtained by the heat treatment step (S6). Step of processing: As the surface smoothing treatment method, cutting methods such as end milling cutting, diamond turning, etc.; grinding method of grinding the surface with a grindstone or the like; honing method such as polishing honing, etc. However, it is not limited to the case where the aluminum alloy thick plate is applied to the vacuum chamber, and the surface smoothing treatment is particularly effective. The reason is as follows. That is, the vacuum chamber-32-200900512 is used to decompress the chamber to a high vacuum. In the case where the gas is adsorbed from the indoor side surface or the gas atoms which are solidified in the thick plate are shown, the degree of vacuum is deteriorated. Therefore, when the target vacuum is reached Therefore, the production efficiency is deteriorated. Based on this, the thickness of the aluminum alloy applied to the chamber is required to be: the gas adsorbed on the surface of the thick plate (on the indoor side) is small, and the formation of a high vacuum still does not release the gas atoms solidified in the thick plate. (B) Method for producing aluminum alloy thick plate according to the fifth to eighth inventions (1) Manufacturing method A method for producing an aluminum alloy thick plate according to the fifth to eighth inventions is as follows, : melting step (S1 ), dehydrogenation (S2 ), filtration step (S3 ), casting step (S4 ), heat treatment (S5 ), cutting step (S6 ), and optionally, surface after cutting (S 6 ) The smoothing treatment step (S7). In the present manufacturing method, first, the aluminum alloy thick plate of the raw material is melted in the melting step (S1). Next, hydrogen gas is removed from the molten aluminum alloy by the hydrogen step (S2). Next, the inclusions of oxides and non-metals and the like are removed by a filtration step. Then, the aluminum alloy casting step (S4) is cast into an ingot. Then, the ingot is heat-treated after heat treatment (S 5 ), The cutting step (S 5 ) is performed to cut the aluminum alloy thick plate of a predetermined thickness. Then, for the aluminum plate of a predetermined thickness 'as needed', the surface smoothing treatment step (S 7 ) is used to smooth the surface. The release plate must be even if the step of the step is stepped out of the step S3). The step is to form the gold thick line table-33-200900512 (2) the wrong alloy in the manufacturing method of the fifth to eighth inventions, as the raw material of the aluminum alloy, A 5,000-series Ai_Mg alloy, a 3,000-series Al-Mn alloy '6000 series Al-Mg-Si alloy, and a 7000 series Al-Zn-Mg alloy were used. The details are explained below. (2-1) Fifth invention The 5000-series Al-Mg alloy which is the same as the first invention is used. The reason why the composition, the component content, and the content of the aluminum alloy are limited is the same as that of the first invention. (2-2) Sixth invention The same 3,000-series Al-Mn alloy as that of the second invention is used. The reason why the composition, the component content, and the content of the aluminum alloy are limited is the same as that of the second invention. (2-3) Seventh invention The 6000-series Al-Mg-Si alloy similar to the third invention is used. The reason why the composition, the component content, and the content of the aluminum alloy are limited is the same as that of the third invention. (2-4) Eighth invention The 7000 series Al-Zn-Mg alloy which is the same as the fourth invention is used. The reason why the composition, the component content, and the content of the aluminum alloy are limited is the same as that of the fourth invention of -34-200900512. (3) Details of Manufacturing Method Next, each step of the manufacturing method of the fifth to eighth inventions will be described in detail. The (3 -1 ) melting step is the same as the melting step (si) of the first to fourth inventions. (3-2) The dehydrogenation step is the same as the dehydrogenation step (S2) of the first to fourth inventions. The (3 - 3) filtration step is the same as the filtration step (S3) of the first to fourth inventions. (3-4) The casting step is the same as the casting step (S4) of the first to fourth inventions. After the ingot obtained by the casting step (S4) is subjected to dicing, the heat treatment step (S 5 ) is carried out, and heat treatment is performed for the purpose of removing internal stress and homogenizing the internal structure. By performing heat treatment on the ingot, the flatness, the thickness accuracy, and the appearance property after the alumite treatment can be improved. (3 - 5) Heat Treatment Step The heat treatment step (S5) is a step of performing heat treatment (homogenization heat treatment) on the _35-200900512 block obtained by the casting step (S4). The heat treatment can be carried out in accordance with a usual method. In other words, the aluminum alloy is a 5,000-series A1-Mg alloy (the fifth invention), the 3000-series Al-Mn alloy (the sixth invention), and the 6000-based Al-Mg-Si alloy (the seventh invention). In the case, the heat treatment is performed by maintaining the temperature at 200 ° C or more and less than 400 ° C for 1 hour or more. Further, in the case where the aluminum alloy is a 7000-series Al-Zn-Mg-based alloy (Eighth Invention), the heat treatment is carried out by maintaining the temperature at 200 ° C or higher and not more than 300 ° C for 1 hour or longer. In the fifth to seventh inventions, when the treatment temperature is less than 200 °C, the amount of internal stress removal is small, and the effect of heat treatment is low. Therefore, the treatment temperature is limited to 200 °C or higher. Further, if the treatment temperature is above 40 °C, the ductility becomes high, and the strength and machinability deteriorate. Machinability represents chip breaking. The chips are preferably broken into small pieces. The reason is that if the chips are long, they will be wound around the processing tool (knife) and rotate together, which will cause the surface of the thick plate to be damaged and the tool to be damaged. Therefore, the treatment temperature is limited to less than 400 °C. By performing heat treatment at such temperature conditions, strength and machinability are not reduced, and flatness and thickness accuracy can be improved. According to the eighth aspect of the invention, when the treatment temperature is less than 200 °C, the amount of internal stress removal is small, and the effect of heat treatment is low. Therefore, the treatment temperature is limited to 200 ° C or more. Further, if the treatment temperature is 550 ° C or higher, the ductility becomes high, and the strength and the machinability deteriorate. Machinability represents chip breaking. The chips are preferably broken into small pieces. The reason is that if the chips are long, they will be wound around the processing tool (knife) and rotate together, which will cause the surface of the thick plate to be damaged and the tool to be damaged. Therefore, the treatment temperature is limited to less than 350 °C. By heat treatment at this temperature -36-200900512, the strength and machinability are not reduced, and the flatness and thickness accuracy can be improved. If the treatment time is less than one hour, the degree of solid solution of the intermetallic compound is insufficient, and the intermetallic compound is easily precipitated. Therefore, the processing time is limited to 1 hour or more. If the treatment time exceeds 8 hours, the effect of the heat treatment is saturated, which will cause energy loss. Therefore, the treatment time should be limited to 8 hours or less. (3-6) Cutting step The cutting step (S 6 ) is a step of cutting the ingot obtained by the heat treatment step (S 5 ) into an aluminum alloy thick plate of a predetermined thickness. The details are the same as the cutting steps (S 5 ) of the first to fourth inventions. The aluminum alloy thick plate after the cutting step (S6) may be subjected to surface smoothing treatment in order to remove crystals and oxides formed on the surface of the thick plate or to suppress gas accumulation on the surface of the thick plate. (3-7) Surface smoothing treatment step The surface smoothing treatment step (S7) is a step of subjecting the surface of the alloy thick plate obtained by the cutting step (S6) to a surface smoothing treatment. The details thereof are the same as those of the surface smoothing processing steps (S7) of the first to fourth inventions. (C) Method for producing aluminum alloy thick plate according to the ninth to twelfthth aspects of the invention (1) Summary of the manufacturing method - 37-200900512 The aluminum alloy thick plate of the ninth to twelfth invention (hereinafter also referred to as "thick plate") The manufacturing method is sequentially performed as shown in Fig. 1 : a melting step (S1), a dehydrogenation step (S2), a filtration step (S3), a casting step (S4), a cutting step (S5), and a heat treatment step ( S6). Further, if necessary, the surface smoothing treatment step (S7) may be performed after the heat treatment step (S6). In the present production method, first, the aluminum alloy thick plate of the raw material is melted in the melting step (S1). Next, hydrogen gas is removed from the molten aluminum alloy by a dehydrogenation step (S2). Next, inclusions such as oxides and non-metals are removed by the filtration step (S3). Next, the aluminum alloy is cast into an ingot at the casting step (S4). Then, the ingot is cut at the cutting step (S 5 ) to form an aluminum alloy thick plate of a predetermined thickness. Then, the aluminum alloy thick plate of a predetermined thickness is thermally buried by the heat treatment step (S6), and then, as needed, the surface smoothing treatment is performed by the surface smoothing treatment step (S7). (2) Aluminum alloy In the manufacturing method of the ninth to twelfth inventions, the "aluminum alloy as a raw material" is a 5000-series Al-Mg alloy, a 3000-series Al-Mn alloy, and a 6000-series Al-Mg-Si system. Alloy and 7000 series Al-Zn-

Mg合金。具體內容說明如下。 (2-1 )第9發明 使用和第1發明相同的5000系之Al-Mg合金。該鋁 -38- 200900512 合金之組成、成分含量、含量之數値限定的理由，都和第 1發明相同。 (2 - 2 )第1 〇發明 使用和第2發明相同的3 000系之A1_Mn合金。該銘 合金之組成、成分含量、含量之數値限定的理由’都和第 2發明相同。 (2-3 )第1 1發明 使用和第3發明相同的6000系之合金。 該鋁合金之組成、成分含量、含量之數値限定的理由’都 和第3發明相同。 (2-4 )第12發明 使用和第4發明相同的7〇〇〇系之Al-Zn-Mg合金。該 鋁合金之組成、成分含量、含量之數値限定的理由，都和 第4發明相同。 (3 )製造方法的詳細 接著詳細說明第9至第1 2發明之製造方法之各步 驟。 (3 -1 )熔解步驟 是和第1至第4發明之熔解步驟（s 1 )相同。 -39- 200900512 (3-2)脫氫氣步驟 是和第1至第4發明之脫氫氣步驟（S2 )相同。 (3 - 3 )過濾步驟 是和第1至第4發明之過濾步驟（S 3 )相同。 (3-4)鑄造步驟 是和第1至第4發明之鑄造步驟（S4 )相同。 (3 - 5 )切割步驟 是和第1至第4發明之切割步驟（S 5 )相同。 (3-6 )熱處理步驟 熱處理步驟（s 6 )，係將切割步驟（S 5 )所得之既定 厚度的鋁合金厚板實施熱處理（均質化熱處理）的步驟。 熱處理可依通常方法來實施。亦即’在鋁合金爲5000系 的Al-Mg系合金（第9發明）、3000系的Al-Mn合金 (第10發明）、6000系的Al-Mg-Si系合金（第11發 明）的情形，是藉由在200°C以上未達400°C的溫度保持1 小時以上來進行熱處理。又在鋁合金是7000系的Al-Zn-Mg系合金（第12發明）的情形，是藉由在200°C以上未 達3 5 0 °C之溫度保持1小時以上來進行熱處理。 在第9至第11發明，若處理溫度未達2 00 °C，內部應 -40- 200900512 力的除去量少，實施熱處理之效果低。因此將處理溫度限 定爲200 °C以上。又若處理溫度爲400 °C以上，延展性變 高，強度和切削性變差。切削性代表切屑斷裂性。切屑以 斷裂成細小爲佳。其原因在於’若切屑長’會纏在加工工 具（刀）上而一起旋轉，如此會造成厚板表面受傷、工具 破損。因此將處理溫度限定爲未達4 0 0 °C。藉由以這種溫 度條件來進行熱處理，不致降低強度和切削性，且能提昇 平坦度及板厚精度。 在第12發明，若處理溫度未達200°C，內部應力的除 去量少，實施熱處理之效果低。因此將處理溫度限定爲 200t以上。又若處理溫度爲35(TC以上，延展性變高，強 度和切削性變差。切削性代表切屑斷裂性。切屑以斷裂成 細小爲佳。其原因在於，若切屑長，會纏在加工工具 (刀）上而一起旋轉，如此會造成厚板表面受傷、工具破 損。因此將處理溫度限定爲未達3 5 0 °C。藉由以這種溫度 條件來進行熱處理，不致降低強度和切削性，且能提昇平 坦度及板厚精度。 若處理時間未達1小時，金屬間化合物之固熔程度不 夠，容易析出金屬間化合物。因此，將處理時間限定爲1 小時以上。又若處理時間超過8小時，熱處理的效果達飽 和，將造成能量損耗。因此宜將處理時間限定爲8小時以 內。 (3-7 )表面平滑化處理步驟 -41 - 200900512 是和第1至第4發明之表面平滑化處理步驟（S7)相 同。 (D )第1 3發明 接著說明本發明的鋁合金厚板。 該鋁合金厚板，係由前述第1至第1 2發明之任一鋁 合金厚板之製造方法所製造出，且具有400 以下的平 均結晶粒徑。 依據本發明之鋁合金厚板，由於平均結晶粒徑爲400 // m以下，可提昇氧化鋁膜處理後之外觀性，又能減少批 次內的參差情形。 若厚板之金屬間化合物的尺寸變大，在進行氧化鋁膜 處理時，厚板的截面及表面會發生不均勻（色調不均）。 然而，依據本發明的鋁合金厚板，由於金屬間化合物的尺 寸小，因此不容易發生不均勻。 關於前述結晶粒徑的測定，例如採用以下方式來進 行。亦即，設鑄塊厚度爲T，從鑄塊的一表面朝另—表面 在厚度T/5、2T/5、3T/5、4T/5計4處的截面，取得測定 値，並求出其平均。這種求測定値的方法，例如可採用切 斷法。在切斷法，是將鋁合金厚板的截面用去皮法触刻 後，用光學顯微鏡來觀察。 關於將平均結晶粒徑控制在4 0 0 /X m以下的方 '法，例j 如可採用以下方法。亦即，將鑄造時的冷卻速度（從液相 線溫度至固相線溫度的平均溫度）設定爲〇.2°C /秒以上。 -42- 200900512 在實施第1至第3發明、第5至第7發明、第 發明的製造方法的情形，藉由使鋁合金含有0 _1 下的Ti或〇·3質量％以下的Zr，能使結晶粒徑 化；又在實施第4發明、第8發明及第12發明 法的情形，藉由使銘合金含有0 · 1質量％以下的’ 質量％以下的Zr，能使結晶粒徑更爲微細化。 藉由前述第1至第12發明的製造方法所製 金厚板，如前述般，由於表面狀態、平坦度及板 好，可適用於各種用途（包括：底基板、搬送裝 裝置用室等的半導體相關裝置；電機電子元件及 置；生活用品；機械零件等等），也能回收使用 途。 又關於鋁合金厚板之耐蝕性，並不構成問題 在於，底基板用厚板和搬送裝置用厚板，由於應 室內，一般不須考慮耐蝕性。又應用於真空裝置 板，由於使用於較少暴露在腐蝕性氣體的環境下 考慮嚴格的耐蝕性。 以上是針對本申請發明的較佳實施形態做說 發明並不限於前述實施形態。 實施例 以下說明本申請發明的實施例。 (1 )第1實施例 9至第1 1 質量％以 更爲微細 之製造方 「i 或 0.25 得的鋁合 厚精度良 置、真空 其製造裝 於其他用 。其理由 用於無塵 用室的厚 ，並不須 明，但本 -43- 200900512 本實施例是關於第1發明。本實施例使用的鋁合金是 5 000系的Al-Mg系合金。 使用表1所示的合金1 A〜1 2 A作爲實施例合金，使 用合金13A〜22A作爲比較例合金。 -44 - 200900512Mg alloy. The details are explained below. (2-1) Ninth invention The 5000-type Al-Mg alloy which is the same as the first invention is used. The reason why the composition, the component content, and the content of the aluminum-38-200900512 alloy are limited is the same as that of the first invention. (2 - 2) The first invention The 3,000-series A1_Mn alloy which is the same as the second invention. The reason why the composition, the component content, and the content of the alloy are limited is the same as that of the second invention. (2-3) Invention No. 1 1 The alloy of the 6000 series which is the same as the third invention is used. The reason why the composition, the component content, and the content of the aluminum alloy are limited is the same as that of the third invention. (2-4) Twelfth invention The same 7-base Al-Zn-Mg alloy as that of the fourth invention is used. The reason why the composition, the component content, and the content of the aluminum alloy are limited is the same as that of the fourth invention. (3) Details of Manufacturing Method Next, each step of the manufacturing method of the ninth to twelfth inventions will be described in detail. The (3 -1 ) melting step is the same as the melting step (s 1 ) of the first to fourth inventions. -39- 200900512 (3-2) The dehydrogenation step is the same as the dehydrogenation step (S2) of the first to fourth inventions. The (3 - 3) filtration step is the same as the filtration step (S 3 ) of the first to fourth inventions. (3-4) The casting step is the same as the casting step (S4) of the first to fourth inventions. (3 - 5) The cutting step is the same as the cutting step (S 5 ) of the first to fourth inventions. (3-6) Heat treatment step The heat treatment step (s 6 ) is a step of subjecting the aluminum alloy thick plate of a predetermined thickness obtained by the cutting step (S 5 ) to a heat treatment (homogenization heat treatment). The heat treatment can be carried out in accordance with a usual method. That is, the Al-Mg-based alloy (the ninth invention) in which the aluminum alloy is 5000 series, the Al-Mn alloy of the 3000 series (the tenth invention), and the Al-Mg-Si alloy of the 6000 series (the eleventh invention) In the case, heat treatment is performed by maintaining the temperature at 200 ° C or more and less than 400 ° C for 1 hour or more. Further, in the case where the aluminum alloy is a 7000-series Al-Zn-Mg-based alloy (12th invention), the heat treatment is carried out by maintaining the temperature at 200 ° C or more and not more than 350 ° C for 1 hour or more. In the ninth to eleventh inventions, if the treatment temperature is less than 200 ° C, the amount of internal force should be -40 - 200900512, and the effect of heat treatment is low. Therefore, the treatment temperature is limited to 200 °C or higher. Further, if the treatment temperature is 400 ° C or more, the ductility becomes high, and the strength and machinability deteriorate. Machinability represents chip breaking. The chips are preferably broken into small pieces. The reason is that if the chip length is entangled on the processing tool (knife) and rotates together, the surface of the slab is injured and the tool is broken. Therefore, the treatment temperature is limited to less than 400 °C. By performing heat treatment at such temperature conditions, strength and machinability are not reduced, and flatness and thickness accuracy can be improved. According to the twelfth aspect of the invention, when the treatment temperature is less than 200 °C, the amount of internal stress removal is small, and the effect of heat treatment is low. Therefore, the treatment temperature is limited to 200 t or more. Further, if the treatment temperature is 35 (TC or more, the ductility becomes high, the strength and the machinability are deteriorated. The machinability represents the chip fracture property. The chip is preferably broken into fine. The reason is that if the chip is long, it will be wrapped around the processing tool. (Knife) rotates together, which will cause damage to the surface of the thick plate and damage the tool. Therefore, the treatment temperature is limited to less than 350 ° C. By heat treatment at this temperature condition, the strength and machinability are not reduced. And can improve the flatness and thickness accuracy. If the treatment time is less than 1 hour, the intermetallic compound is not solid enough to precipitate the intermetallic compound. Therefore, the treatment time is limited to 1 hour or more. After 8 hours, the effect of the heat treatment is saturated, which will cause energy loss. Therefore, the treatment time should be limited to 8 hours. (3-7) Surface smoothing treatment step -41 - 200900512 is the surface smoothing with the first to fourth inventions The treatment step (S7) is the same. (D) The first aspect of the invention is the aluminum alloy thick plate according to the present invention. The aluminum alloy thick plate is any one of the first to the second inventions. The method for producing a thick plate has an average crystal grain size of 400 or less. According to the aluminum alloy thick plate of the present invention, since the average crystal grain size is 400 // m or less, the appearance of the aluminum oxide film can be improved. In addition, if the size of the intermetallic compound in the thick plate becomes large, the cross section and surface of the thick plate may be uneven (uneven in color tone) when the aluminum oxide film is processed. In the aluminum alloy thick plate of the present invention, since the size of the intermetallic compound is small, unevenness is less likely to occur. The measurement of the crystal grain size is carried out, for example, in the following manner, that is, the thickness of the ingot is set to T, from casting. One surface of the block is measured at a cross section of the other surface at thicknesses T/5, 2T/5, 3T/5, and 4T/5, and the average is obtained, and the method for determining the enthalpy is, for example, The cutting method can be used. In the cutting method, the cross section of the aluminum alloy thick plate is touched by a peeling method, and then observed by an optical microscope. The average crystal grain size is controlled to be 400 or less. 'Law, example j can be used as follows That is, the cooling rate at the time of casting (the average temperature from the liquidus temperature to the solidus temperature) is set to 0.2 ° C / sec or more. -42 - 200900512 In the implementation of the first to third inventions, In the case of the production method of the fifth invention and the seventh aspect of the invention, the aluminum alloy may contain Ti of 3-1 or 3% by mass or less of Zr, and the crystal grain size may be increased. In the case of the invention of the first and twelfth aspects, the crystal grain size can be made finer by making the alloy containing 0% by mass or less of Z% by mass or less. As described above, the gold plate produced by the manufacturing method can be applied to various applications (including a substrate-related device such as a base substrate and a transfer device), and a motor electronic component and a device, because of a surface condition, a flatness, and a good plate; Daily necessities; mechanical parts, etc.) can also be recycled. Further, the corrosion resistance of the aluminum alloy thick plate does not pose a problem in that the thick plate for the base substrate and the thick plate for the conveying device do not have to be considered for corrosion resistance in the room. It is also applied to vacuum panels due to the strict corrosion resistance used in environments exposed to less corrosive gases. The above is a description of the preferred embodiments of the present invention. The invention is not limited to the embodiments described above. EXAMPLES Examples of the invention of the present application will be described below. (1) The first embodiment 9 to the first 1% by mass are made of a finer aluminum alloy having a thickness of "i or 0.25", and the vacuum is manufactured and used for other purposes. The reason is for a dust-free chamber. The thickness of the present invention is not limited, but this embodiment relates to the first invention. The aluminum alloy used in the present embodiment is a 5,000-series Al-Mg-based alloy. The alloy 1 A shown in Table 1 is used. ~1 2 A As the alloy of the example, alloys 13A to 22A were used as alloys of the comparative example. -44 - 200900512

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V6W VOl啪啦 νιι^φ ν(Νι^&lt;π VU&lt;^&lt;π V寸一領4Π νςι&lt;^&lt;π Υ9ι&lt;^&lt;π V卜一領&lt;π V8I 領&lt;π V6I 領&lt;π νο(Ν^&lt;π νι(Ν&lt;^&lt;π V(NI(NI領&lt;πι -45- 200900512 (處理） 首先，將合金1A〜22A依序進行熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟之處理，製作出板厚50 〇mm 的鑄塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割 材，係將前述鑄塊經由切割步驟的處理而製得。熱壓延 材，是將前述鑄塊熱處理後進行熱壓延而製得。切割材和 熱壓延材，都是厚度20mmx寬度lOOOmmx長度2000mm的 鋁合金厚板。 接著，將前述切割材用熱處理步驟進行處理。亦即， 將前述切割材在50(TC保持4小時。 因此，前述處理後的切割材就是第1發明的製造方法 所製得之鋁合金厚板，但前述處理後的熱壓延材並不是。 只有使用合金1A〜22A之切割材才是屬於第1發明的實 施例。 接著，對前述處理後之切割材和熱壓延材進行以下的 試驗。 &lt;平坦性評價試驗&gt; 平坦性評價，是對切割材，測定鑄造方向每1 m的彎 曲量（平坦度），對於熱壓延材，則是測定壓延方向每 1 m的彎曲量（平坦度）。平坦度爲0 · 4mm/1 m長以下的情 形判定爲合格（〇），超過〇.4mm/lm長的情形判定爲不 合格（X )。 -46 - 200900512 &lt;板厚精度評價試驗&gt; 板厚精度評價，是用測微計測定6個部位的厚度。6 個部位包括：厚板的4隅，從厚板的長邊方向的一半長度 的部分朝寬方向內側20mm的部位。當6個部位全部都在 19.94mm〜20.06mm的情形判定爲良好（◎)，都在 1 9.9 0mm〜2 0 · 1 0mm的情形判定爲合格（〇）。 &lt;強度試驗&gt; 強度試驗是依下述方式來進行。亦即，從鋁合金厚板 製作出JIS 5號的試驗片，用該試驗片進行拉伸試驗，測 定拉伸強度及0.2%安全限應力。拉伸強度爲180N/mm2以 上的情形判定爲合格（〇），拉伸強度未達1 80N/mm2的 情形判定爲不合格（X )。 &lt;氧化鋁膜處理性評價試驗&gt; 氧化鋁膜處理性評價，是依下述方式來進行。在鋁合 金厚板的表面及截面，藉由硫酸氧化鋁膜處理，形成厚度 1 〇 # m的氧化鋁皮膜。處理條件爲丨5%硫酸、20°C、電流 密度2A/dm2。觀察厚板的表面及截面的外觀。外觀未發 生不均勻（色調不均）的情形判定爲合格（〇），發生不 均句的情形判定爲不合格（X )。 由於厚板的結晶粒徑會影響氧化鋁膜處理性，故求出 厚板的平均結晶粒徑。平均結晶粒徑的測定是採用下述方 -47- 200900512 式來進行。亦即，設鋁合金厚板的厚度爲 表面朝另一表面在厚度T/5、2175、3T/5、 截面，取得測定値，並求出其平均。這 法’例如可採用切斷法。在切斷法，是將 面用去皮法蝕刻後，用光學顯微鏡來觀察 試驗結果顯示於表2及表3。 T，從厚板的一 4T/5計4處的 重求測定値的方 鋁合金厚板的截 -48- 200900512 I# ?7y) -iif 081 081V6W VOl啪啦νιι^φ ν(Νι^&lt;π VU&lt;^&lt;πV inch one collar 4Π νςι&lt;^&lt;π Υ9ι&lt;^&lt;π V卜一领&lt;π V8I collar&lt;π V6I Collar &lt;π νο(Ν^&lt;π νι(Ν&lt;^&lt;π V(NI(NI collar&lt;πι -45- 200900512 (Processing) First, the alloy 1A~22A is sequentially melted, dehydrogenated In the step of the step, the filtration step and the casting step, an ingot having a thickness of 50 〇 mm is produced. Next, a cutting material and a hot rolled material are produced from the ingot, and the cutting material is processed by the cutting step. The hot rolled product is obtained by heat-treating the ingot and heat-treating the same. The cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. The cutting material is treated by a heat treatment step, that is, the cutting material is held at 50 (TC for 4 hours. Therefore, the cut material after the treatment is the aluminum alloy thick plate obtained by the manufacturing method of the first invention, but the foregoing treatment The latter hot rolled material is not. Only the cutting material using the alloys 1A to 22A is an embodiment belonging to the first invention. Next, the following test was performed on the cut material and the hot rolled material after the above treatment. <Flatness evaluation test> Flatness evaluation was performed to measure the amount of bending (flatness) per 1 m in the casting direction for the cut material. For the hot rolled material, the amount of bending (flatness) per 1 m in the rolling direction is measured. When the flatness is 0 · 4 mm / 1 m or less, it is judged as qualified (〇), and exceeds 〇.4 mm/lm long. The case was judged to be unacceptable (X). -46 - 200900512 &lt;Thickness Accuracy Evaluation Test&gt; The thickness evaluation was performed by measuring the thickness of six parts with a micrometer. The six parts included: 4 sheets of thick plates. , from the half length of the long side of the thick plate to the inner side of the width direction of 20 mm. When all the six parts are in the range of 19.94 mm to 20.06 mm, it is judged as good (◎), both at 1 9.9 0 mm~2 0 In the case of 10 mm, it was judged as pass (〇). &lt;Strength test&gt; The strength test was carried out in the following manner. That is, a test piece of JIS No. 5 was produced from an aluminum alloy thick plate, and the test piece was used for the test piece. Tensile test to determine tensile strength and 0.2% safety limit stress. Tensile When the strength was 180 N/mm2 or more, it was judged as pass (〇), and when the tensile strength was less than 180 N/mm2, it was judged as unacceptable (X). &lt;Alumina film treatability evaluation test&gt; Alumina film treatability The evaluation was carried out in the following manner: An aluminum oxide film having a thickness of 1 〇 # m was formed on the surface and cross section of the aluminum alloy thick plate by an alumina sulfate film treatment. The treatment conditions were 丨 5% sulfuric acid, 20 ° C, and current density 2 A/dm 2 . Observe the appearance of the surface and section of the slab. The case where the appearance was not uneven (uneven unevenness) was judged as pass (〇), and the case where the uneven sentence occurred was judged as unacceptable (X). Since the crystal grain size of the thick plate affects the handleability of the alumina film, the average crystal grain size of the thick plate is determined. The measurement of the average crystal grain size was carried out by the following formula -47-200900512. That is, the thickness of the aluminum alloy thick plate is such that the surface faces the other surface at thicknesses T/5, 2175, 3T/5, and the cross section, and the measurement enthalpy is obtained, and the average is obtained. This method 'for example, a cutting method can be employed. In the cutting method, the surface was etched by peeling and observed by an optical microscope. The test results are shown in Tables 2 and 3. T, from the slab of a 4T/5 meter 4 to re-determine the side of the aluminum alloy thick plate cut -48- 200900512 I# ?7y) -iif 081 081

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I εζ/ο 02 οςο osd (Nsd osd ε寸ο i i ISO(Nlsol ISO (N!s(NI2 I「o(Nlsol § ¥i ν5&lt;π ν(Ν^&lt;π νε 領&lt;π V寸領&lt;π ν$&lt;π &lt;;9領&lt;0 V卜姻4Π V8&lt;^&lt;n V6^&lt;n V0I 領&lt;π VII 領φ WI領如 να 領&lt;0 νι&lt;ΝΙ^ιφι vo(NI領&lt;nl V6l^l4nl V8I&lt;^l&lt;nl V卜1領如 V9I 領4ΠΙ νιηιΙ^ιφι VH 領&lt;πι § -50- 200900512 表2顯示切割材之試驗結果。表2中’合金1 A〜1 2 A 屬於實施例，合金〜22A屬於比較例。表3顯示熱壓 延材的試驗結果。表3中’合金1 A〜22A全都屬於比較 例。 (關於切割材） 如表2所示’在合金1A〜13A、合金15A〜22A的情 形，加工應變少’彎曲小。亦即平坦度良好。又板厚精度 良好。 在合金1 4 A的情形，由於M g含量超過上限値，會發 生鑄造裂痕，無法進行製造。在合金1 3 A的情形，由於 Mg含量未達下限値，其強度不足。 在合金1A〜13A、17A、20A〜22A的情形，氧化銘膜 處理後的表面外觀未發生不均勻。在合金15A、16A、 1 8 A、1 9 A各個的情形，由於S i、F e、Μ η、C r含量分別超 過上限値，會生成粗大的金屬間化合物，氧化鋁膜處理後 的表面外觀會發生不均勻。在合金1A〜13A、15A〜22A 的情形，氧化鋁膜處理後的表面外觀不會發生不均勻。 又在合金17A、20A、21A、22A各個的情形，由於 Cu、Zn、Ti、Zr的含量分別超過上限値，其等的效果達 飽和，故經濟性不佳。 (關於熱壓延材） 如表3所示，在合金1 A〜1 3 A、1 5 A〜2 2 A的情形， -51 - 200900512 會累積加工應變，壓延方向的彎曲大。亦即平坦度不佳。 又板厚精度比起切割材，幾乎都比較差。 在合金14A的情形，由於Mg含量超過上限値，會發 生鑄造裂痕，無法進行製造。在合金1 3 A的情形，由於 Mg含量未達下限値，其強度不足。 在合金15A、16A、18A、19A各個的情形，由於Si、 Fe、Μη、Cr含量分別超過上限値，會生成粗大的金屬間 化合物，氧化鋁膜處理後的表面外觀會發生不均勻。在合 金1A〜13A、15A〜22A的情形，氧化鋁膜處理後的表面 外觀發生不均句。 (2 )第2實施例 本實施例是關於第1發明。在本實施例，是使用表1 所示的合金3 A。 (處理） 首先，將合金3 A依序經由熔解步驟、脫氫氣步驟、 過濾步驟及鑄造步驟的處理，製作出板厚50 0mm的鑄 塊。 接著’將前述鑄塊藉由切割步驟的處理來獲得切割 材。切割材爲厚度20mmx寬度lOOOmmx長度2000mm的銘 合金厚板。 接著’將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材用表4所示的條件進行熱處理。 -52- 200900512 [表4] 區分 編號 均質化熱處理 平坦度 板厚精度 (mm/m) 判定 判定 實施例 A1 合金3A 420°Cx2 小時 0.21 ◎ ◎ 切 A2 合金3A 500°Cx4 小時 0.19 ◎ ◎ 割 A3 合金3A Μ 0.30 〇 〇 材 比較例 A4 合金3A 380°Cx4 小時 0.26 〇 ◎ A5 合金3A 530〇Cx2 小時 發生熔毀(burning),無法進行製造 因此，熱處理條件符合第1發明之A1及A2，是屬於 第1發明的實施例；熱處理條件不符合第1發明的A3〜 A 5，是屬於比較例。 對於前述處理後的切割材，進行平坦性評價試驗及板 厚精度評價試驗。 &lt;平坦性評價試驗&gt; 平坦性評價，是測定鑄造方向每1 m的彎曲量（平坦 度），平坦度爲 〇.4mm/lm長以下的情形判定爲合格 (〇），在〇 . 2 5 mm/1 m長以下的情形判定爲良好（◎)。 &lt;板厚精度評價試驗&gt; 關於板厚精度評價試驗，是和第1實施例的情形相 同。 試驗結果顯示於表4。 如表4所示，實施例A1、A2之熱處理條件符合第1 -53- 200900512 發明，因此平坦度及板厚精度良好。又在比較例A3，由 於未進行熱處理，比起實施例A1、A2，其平坦度及板厚 精度稍差。在比較例A4，由於處理溫度比第1發明的範 圍更低（未達4 0 0 °C )，比起實施例 A1、A2 ’其平坦度 稍差。又在比較例A5，由於處理溫度比第1發明的範圍 更高（超過熔點），在內部發生局部熔融而形成內部缺 陷，因此無法獲得製品。 (3 )第3實施例 本實施例是關於第2發明。本實施例使用的鋁合金爲 3000系的Al-Mn合金。 使用表5所示的合金23 A、24A作爲實施例合金，使 用合金25A、26A作爲比較例合金。 表5] 區分 編號 元素(質量％) 合金 種類 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr 實施例 合金 合金23A - 0.1 0.3 - 0.5 — - 0.01 - 3000 系 合金24A - 0.1 0.4 - 0.9 - - 0.01 - 3000 系 比較例 合金 合金25A - 0.1 0.4 - 0.2 - - 0.01 - 3000 系 Μη未達下限値 合金26A - 0.1 0.3 - 1.7 ~ - 0.01 0.1 3000 系 Μη超過上限値 (處理） 首先，將合金23 A〜26A依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理，製作出板厚500mm 的鑄塊。 -54- 200900512 接著，從前述鑄塊製作出切割材和熱壓延材。切割材 是將前述鑄塊經由切割步驟處理所得。熱壓延材’是將前 述鑄塊熱處理後進行熱壓延而製得。切割材和熱壓延材都 是厚度20mmx寬度lOOOmmx長度2000mm的鋁合金厚板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材在50(TC保持4小時。 因此，前述處理後的切割材是屬於第2發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金23 A、24A之切割材屬於第2發明的實施 例。 接著，對於前述處理後的切割材及熱壓延材，進行平 坦性評價試驗、板厚精度評價試驗、強度試驗以及氧化鋁 膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的ΐ平價 基準如下。亦即，在強度方面，將拉伸強度9〇N/mm2以上 的情形判定爲合格（〇），將拉伸強度未達9 0 N / m m 2的情 形判定爲不合格（X )。 試驗結果顯示於表6。 -55- 200900512 1蝤—— 〇 ~οι— ~~δ~ δ~~ 0^00 騷忒晅嗽 〇 d, 〇 d,I εζ/ο 02 οςο osd (Nsd osd ε inch ο ii ISO (Nlsol ISO (N!s(NI2 I"o(Nlsol § ¥i ν5&lt;π ν(Ν^&lt;π νε collar&lt;π V inch collar &lt;π ν$&lt;π &lt;;9 collar&lt;0 V Buxue 4Π V8&lt;^&lt;n V6^&lt;n V0I collar&lt;π VII collar φ WI collar as να collar&lt;0 νι&lt;ΝΙ ^ιφι vo(NI collar&lt;nl V6l^l4nl V8I&lt;^l&lt;nl VBu 1 collar such as V9I collar 4ΠΙ νιηιΙ^ιφι VH collar&lt;πι § -50- 200900512 Table 2 shows the test results of the cut material. Table 2 The alloys 1 A to 1 2 A belong to the examples, and the alloys ~22A belong to the comparative examples. Table 3 shows the test results of the hot rolled materials. In Table 3, 'alloys 1 A to 22A are all comparative examples. (About cutting materials) As shown in Table 2, in the case of alloys 1A to 13A and alloys 15A to 22A, the processing strain is small, and the bending is small, that is, the flatness is good, and the plate thickness precision is good. In the case of alloy 1 4 A, due to the Mg content. When the upper limit is exceeded, casting cracks may occur and manufacturing is impossible. In the case of alloy 13 A, the strength is insufficient because the Mg content is less than the lower limit. In the case of alloys 1A to 13A, 17A, 20A to 22A, the oxide film is oxidized. deal with The appearance of the surface is not uneven. In the case of alloys 15A, 16A, 18A, and 19 A, since the contents of S i, F e, η η, and Cr exceed the upper limit, respectively, coarse intermetallic compounds are formed. The surface appearance after the treatment of the aluminum oxide film may be uneven. In the case of the alloys 1A to 13A and 15A to 22A, the surface appearance after the treatment of the aluminum oxide film does not occur unevenly. Also in the alloys 17A, 20A, 21A, 22A In each case, since the contents of Cu, Zn, Ti, and Zr exceed the upper limit, respectively, the effects of the above are saturated, so the economy is not good. (About the hot rolled material) As shown in Table 3, in the alloy 1 A~ In the case of 1 3 A, 1 5 A to 2 2 A, -51 - 200900512 will accumulate machining strain, and the bending in the rolling direction is large, that is, the flatness is not good. The thickness accuracy is almost inferior to that of the cutting material. In the case of the alloy 14A, since the Mg content exceeds the upper limit 铸造, casting cracks occur and manufacturing cannot be performed. In the case of the alloy 13 A, since the Mg content does not reach the lower limit 値, the strength is insufficient. In the alloys 15A, 16A, 18A, 19A in each case, due to Si, Fe, Μη, Cr When the amount exceeds the upper limit, a coarse intermetallic compound is formed, and the surface appearance of the aluminum oxide film is uneven. In the case of the alloys 1A to 13A and 15A to 22A, the appearance of the surface after the treatment of the alumite film was uneven. (2) Second Embodiment This embodiment relates to the first invention. In the present embodiment, the alloy 3 A shown in Table 1 was used. (Treatment) First, the alloy 3 A was sequentially subjected to a melting step, a dehydrogenation step, a filtration step, and a casting step to prepare a cast piece having a thickness of 50 mm. Next, the cutting block is obtained by the treatment of the cutting step. The cutting material is a thick alloy plate with a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cut material is treated by a heat treatment step. Namely, the above-mentioned cut material was heat-treated under the conditions shown in Table 4. -52- 200900512 [Table 4] Classification No. Homogenization Heat Treatment Flatness Thickness Accuracy (mm/m) Judgment Determination Example A1 Alloy 3A 420 °C x 2 hours 0.21 ◎ ◎ Cut A2 Alloy 3A 500 °C x 4 hours 0.19 ◎ ◎ Cut A3 Alloy 3A Μ 0.30 Coffin Comparative Example A4 Alloy 3A 380 ° C x 4 hours 0.26 〇 ◎ A5 Alloy 3A 530 〇 Cx2 hours of burning, cannot be manufactured. Therefore, the heat treatment conditions are in accordance with A1 and A2 of the first invention. The embodiment according to the first invention is not in conformity with A3 to A5 of the first invention, and is a comparative example. For the cut material after the above treatment, a flatness evaluation test and a thickness evaluation test were performed. &lt;Flatness evaluation test&gt; The flatness evaluation was performed by measuring the amount of bending (flatness) per 1 m in the casting direction, and the flatness was 〇.4 mm/lm or less, and it was judged as pass (〇), in 〇. 2 The case of 5 mm/1 m or less was judged to be good (?). &lt;Thickness Accuracy Evaluation Test&gt; The thickness evaluation test was the same as in the first embodiment. The test results are shown in Table 4. As shown in Table 4, the heat treatment conditions of Examples A1 and A2 were in accordance with the invention of No. 1 -53 to 200900512, and therefore the flatness and the plate thickness were excellent. Further, in Comparative Example A3, since the heat treatment was not performed, the flatness and the sheet thickness accuracy were slightly inferior to those of Examples A1 and A2. In Comparative Example A4, since the treatment temperature was lower than that of the first invention (less than 4,000 °C), the flatness was slightly inferior to those of Examples A1 and A2'. Further, in Comparative Example A5, since the treatment temperature was higher than the range of the first invention (exceeding the melting point), local melting occurred inside and internal defects were formed, so that the product could not be obtained. (3) Third Embodiment This embodiment relates to the second invention. The aluminum alloy used in this embodiment is a 3000-series Al-Mn alloy. Alloys 23 A and 24A shown in Table 5 were used as the alloys of the examples, and alloys 25A and 26A were used as the alloys of the comparative examples. Table 5] Distinguished number element (% by mass) Alloy type Preparation Mg Si Fe Cu Μη Cr Zn Ti Zr Example Alloy alloy 23A - 0.1 0.3 - 0.5 — - 0.01 - 3000 Alloy 24A - 0.1 0.4 - 0.9 - - 0.01 - 3000 Comparative alloy alloy 25A - 0.1 0.4 - 0.2 - - 0.01 - 3000 Μ 未 未 未 値 26 26 26A - 0.1 0.3 - 1.7 ~ - 0.01 0.1 3000 Μ 超过 exceeds the upper limit 处理 (treatment) First, the alloy 23 A~26A An ingot having a thickness of 500 mm was produced through a melting step, a dehydrogenation step, a filtration step, and a casting step. -54- 200900512 Next, a cutting material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material 'is obtained by heat-treating the ingot described above and then hot rolling. Both the cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. That is, the cutting material is held at 50 (TC for 4 hours. Therefore, the cut material after the treatment is an aluminum alloy thick plate obtained by the manufacturing method of the second invention, and the heat-rolled material after the treatment is not Only the cutting materials using the alloys 23 A and 24A belong to the embodiment of the second invention. Next, the flatness evaluation test, the thickness evaluation test, the strength test, and the flatness test and the hot rolled material after the treatment are performed. Alumina film treatability evaluation test The method and evaluation criteria of each test are the same as in the case of the first embodiment. Since the thickness characteristics vary depending on the type of the alloy, the strength of the barium parity is as follows. On the other hand, the case where the tensile strength was 9 〇N/mm 2 or more was judged as pass (〇), and the case where the tensile strength was less than 90 N / mm 2 was judged as unacceptable (X). The test results are shown in Table 6. -55- 200900512 1蝤—— 〇~οι— ~~δ~ δ~~ 0^00 Sao d, 〇d,

X i4 〇X i4 〇

X 〇X 〇

I 0卜Ti Ιί {Slm/M} 8U ^一~~ (SIS/N} 侧截«-i 码「14I 0卜 Ti Ιί {Slm/M} 8U ^一~~ (SIS/N} Side cut «-i code "14

〇 W W &quot;W 〇〇 W W &quot;W 〇

XX

XX

X {ui/mm} 黯躍 5寸Ό I寸Ό CNI寸 Ό 1寸.0 寸Γ0 6Γ0 Is 61Ό V 寸(Ν^&lt;π νε(Ν領&lt;π □ ν9&lt;Ν&lt;^&lt;π V93 領&lt;0νς(Ν領&lt;0 ν 寸(Ν領&lt;0 區分 {_辑匡 綠Mi]閲智 -56- 200900512 (關於切割材） 如表6所示，在合金2 3 A〜2 6 A的情形，加工 小，彎曲小。亦即平坦度良好，又板厚精度優異。 在合金25A的情形，由於Μη含量未達下限値’ 不足。在合金26Α的情形，由於Μη含量超過上限値 生成粗大的金屬間化合物，氧化鋁膜處理後的表面外 生不均勻。在合金23Α〜26Α的情形，在氧化鋁膜處 的截面外觀不會發生不均勻。 (關於熱壓延材） 如表6所示，在合金23Α〜26Α的情形，會累積 應變，壓延方向的彎曲大。亦即平坦度不佳。又板厚 比起切割材，幾乎都比較差。 在合金2 5 Α的情形，由於Μη含量未達下限値， 其他的熱壓延材，其強度稍差。在合金26Α的情形， Μη含量超過上限値，會生成粗大的金屬間化合物， 化鋁膜處理後的表面外觀發生不均勻。在合金23Α〜 的情形，氧化鋁膜處理後的截面外觀發生不均勻。 (4 )第4實施例 本實施例是關於第3發明。本實施例使用的鋁合 6000系的Al-Mg-Si系合金。 使用表7所示的合金27A、28A作爲實施例合金 用合金29A〜32A作爲比較例合金。 應變 強度 ，會 觀發 理後X {ui/mm} 5 5 5 inch Ό I inch Ό CNI inch Ό 1 inch. 0 inch Γ 0 6Γ0 Is 61Ό V inch (Ν^&lt;π νε(Ν领&lt;π □ ν9&lt;Ν&lt;^&lt;π V93 collar &lt;0νς(Ν领&lt;0 ν inch (Ν collar&lt;0 distinction {_编匡绿Mi]阅智-56- 200900512 (about cutting material) as shown in Table 6, in alloy 2 3 A~ In the case of 2 6 A, the processing is small and the bending is small, that is, the flatness is good, and the plate thickness precision is excellent. In the case of the alloy 25A, since the Μη content is not lower than the lower limit 値' is insufficient. In the case of the alloy 26Α, since the Μη content exceeds The upper limit 値 generates a coarse intermetallic compound, and the surface of the aluminum oxide film is exogenously uneven. In the case of the alloy 23 Α to 26 Α, the cross-sectional appearance at the aluminum oxide film does not become uneven. (About hot rolled material) As shown in Table 6, in the case of the alloy 23Α~26Α, the strain is accumulated, and the bending in the rolling direction is large, that is, the flatness is not good. The thickness of the plate is almost inferior to that of the cutting material. In the alloy 2 5 Α In the case, since the Μη content does not reach the lower limit 値, the other hot rolled materials have a slightly weaker strength. In the case of the alloy 26 ,, the Μη content is super When the upper limit is exceeded, a coarse intermetallic compound is formed, and the surface appearance after the aluminum film treatment is uneven. In the case of the alloy 23Α, the cross-sectional appearance of the aluminum oxide film after treatment is uneven. (4) Fourth embodiment This embodiment relates to the third invention. The Al-Mg-Si alloy of the aluminum alloy 6000 type used in the present embodiment. The alloys 27A and 28A shown in Table 7 are used as the alloys for the alloys of the examples as the comparative alloys 29A to 32A. Strain strength, after the treatment

加工 精度 比起 由於 在氧 26A 金是 ，使 -57- 200900512 [表7] 區分 編號 元素&lt; 〔質量％) 合金種 類 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr 實 施合 例金 合金27A 1.0 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 6000 系 合金28A 0.5 1.0 0.2 - 0.1 - - 0.02 - 6000 系 比 例 合 S 合金29A 0.9 0.1 0.5 - 0.1 一 - 0.02 一 6000 系 Si未達下限値 合金30A 0.9 1.8 0.4 一 0.1 - - 0.02 — 6000 系 Si超過上限値 合金31A 0.2 0.5 0.5 0.1 一 0.02 - 6000 系 Mg未達下限値 合金32A 1.7 0.5 0.4 0.1 一 0.02 - 6000 系 Mg超過上限値 (處理） 首先，將合金27A〜32A依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理，製作出板厚5 00mm 的鑄塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割材 是將前述鑄塊經由切割步驟處理所得。熱壓延材，是將前 述鑄塊熱處理後進行熱壓延而製得。切割材和熱壓延材都 是厚度20mmx寬度lOOOmmx長度2000mm的鋁合金厚板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材在5 00°C保持4小時。 進一步，將製得的切割材及熱壓延材以520°C進行熔 體化處理，然後以1 7 5 °c進行8小時的時效處理。 因此，前述處理後的切割材是屬於第3發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金27A、28A之切割材屬於第3發明的實施 例。 -58- 200900512 接著，對於前述處理後的切割材及熱壓延材，進行強 度試驗以及氧化鋁膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度200N/mm2以 上的情形判定爲合格（〇），將拉伸強度未達200N/mm2 的情形判定爲不合格（X )。 試驗結果顯示於表8。 [表8]The processing accuracy is compared with that due to the oxygen in the 26A gold, so that -57- 200900512 [Table 7] distinguishes the numbering element &lt; [% by mass] Alloy type Preparation Mg Si Fe Cu Μ Cr Cr Zn Ti Zr Implementation of the joint gold alloy 27A 1.0 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 6000 series alloy 28A 0.5 1.0 0.2 - 0.1 - - 0.02 - 6000 series ratio S alloy 29A 0.9 0.1 0.5 - 0.1 a - 0.02 a 6000 series Si not reached the lower limit 値 alloy 30A 0.9 1.8 0.4 a 0.1 - - 0.02 — 6000 Si exceeds the upper limit 値 alloy 31A 0.2 0.5 0.5 0.1 0.02 - 6000 Series Mg not reached the lower limit 値 alloy 32A 1.7 0.5 0.4 0.1 0.02 - 6000 Series Mg exceeds the upper limit 处理 (treatment) First, the alloy 27A~32A An ingot having a thickness of 500 mm was produced through a melting step, a dehydrogenation step, a filtration step, and a casting step. Next, a cut material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by heat-treating the ingot described above and then hot rolling. Both the cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. That is, the above cut material was kept at 500 ° C for 4 hours. Further, the obtained cut material and hot rolled material were melted at 520 ° C, and then aged at 175 ° C for 8 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the third invention, and the hot rolled material after the above treatment is not. Further, only the cutting materials using the alloys 27A and 28A belong to the embodiment of the third invention. -58-200900512 Next, the strength test and the alumina film treatability evaluation test were performed on the cut material and the hot rolled material after the above treatment. The method and evaluation criteria of each test were the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the strength evaluation criteria are as follows. In other words, in terms of strength, the tensile strength of 200 N/mm2 or more was judged as pass (〇), and the tensile strength of less than 200 N/mm2 was judged as unacceptable (X). The test results are shown in Table 8. [Table 8]

區分 編號 強度 氧化鋁膜處理後外觀 拉伸強度 (N/mm2) 安全限應力 (N/mm2) 判定 表面外觀 截面外觀 切 實 施 例 合金27Α 322 272 〇 〇 〇 合金28Α 296 250 〇 〇 〇 割 比 合金29Α 114 67 X 〇 〇 材 合金30Α 342 302 〇 X 〇 較 /7：ιί 合金31A 178 125 X 〇 〇 例 合金32A 210 124 〇 〇 〇 合金27A 346 276 〇 〇 X 熱 比 合金28A 318 276 〇 〇 X 壓 合金29A 138 88 X 〇 X 延 較 /7：ίΓ 合金30A 365 323 〇 X X 材 例 合金31A 197 143 X 〇 X 合金32A 235 146 〇 〇 X (關於切割材） -59- 200900512 如表8所示’在合金29A、31A的情形，由於Si、Mg 含量分別未達下限値，強度不足。在合金3 0 A的情形，由 於S i含量超過上限値，會生成粗大的金屬間化合物，氧 化鋁膜處理後的表面外觀發生不均勻。在合金32A的情 形’由於Mg含量超過上限値，Mg效果達飽和，經濟性 差。在合金27A〜32A的情形，在氧化鋁膜處理後的截面 外觀不會發生不均勻。 (關於熱壓延材） 如表8所示’在合金29 A、3 1A的情形，由於Si、Mg 含量分別未達下限値，強度不足。在合金3 0 A的情形，由 於S i含量超過上限値，會生成粗大的金屬間化合物，氧 化鋁膜處理後的表面外觀發生不均勻。在合金32A的情 形’由於M g含量超過上限値，M g效果達飽和，經濟性 差。在合金2 7 A〜3 2 A的情形，在氧化鋁膜處理後的截面 外觀會發生不均句。 (5 )第5實施例 本實施例是關於第4發明。本實施例使用的鋁合金， 是7000系的Al-Zn-Mg系合金。 使用表9所示的合金33A、34A作爲實施例合金，使 用合金35A〜38A作爲比較例合金。 -60- 200900512 [表9] 區分 編號 元素(質量％) 合金 種類 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr 晨合 例金 合金33A 2.5 0.1 0.2 1.8 - 0.2 5.5 0.02 - 7000 系 合金34A 3.5 0.2 0.2 2.0 - - 8.5 0.02 0.2 7000 系 比 例 合 I 合金35A 0.3 0.1 0.2 2.2 - 0.1 4.0 0.02 - 7000 系 Mg未達下限値 合金36A 5.0 0.2 0.2 2.0 - 0.1 5.0 0.02 - 7000 系 Mg超過卜限値 合金37A 2.5 0.1 0.2 2.2 - 0.1 2.4 0.02 - 7000 系 Zn未達下限値 合金38A 3.0 0.2 0.2 2.0 - 0.1 9.5 0.02 - 7000 系 Zn超過上限値 (處理） 首先，將合金33A〜38A依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理，製作出板厚5 00mm 的鑄塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割材 是將前述鑄塊經由切割步驟處理所得。熱壓延材，是將前 述鑄塊熱處理後進行熱壓延而製得。切割材和熱壓延材都 是厚度20mmx寬度lOOOmmx長度2000mm的鋁合金厚板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材在5 0 0 °C保持4小時。 進一步，將製得的切割材及熱壓延材以4 7 0 °C進行熔 體化處理，然後以1 2 0 °C進行4 8小時的時效處理。 因此，前述處理後的切割材是屬於第4發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金33 A、34A之切割材屬於第4發明的實施 例。 接著，對於前述處理後的切割材及熱壓延材，進行強 -61 - 200900512 度試驗以及氧化鋁膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度2 50N/mm2以 上的情形判定爲合格（〇），將拉伸強度未達2 5 0N/mm2 的情形判定爲不合格（X )。 試驗結果顯示於表1 〇。 [表 1〇]Distinguishing the tensile strength of the numbered strength of the alumina film after treatment (N/mm2) Safety limit stress (N/mm2) Judging the appearance of the appearance of the surface section Example alloy 27Α 322 272 〇〇〇 alloy 28Α 296 250 castration alloy 29Α 114 67 X Coffin alloy 30Α 342 302 〇X 〇/7: ιί Alloy 31A 178 125 X 〇〇Example alloy 32A 210 124 〇〇〇 alloy 27A 346 276 〇〇X heat ratio alloy 28A 318 276 〇〇X Pressed alloy 29A 138 88 X 〇X extended /7: Γ 合金 alloy 30A 365 323 〇 XX material alloy 31A 197 143 X 〇X alloy 32A 235 146 〇〇X (on cutting material) -59- 200900512 as shown in Table 8 In the case of Alloys 29A and 31A, since the Si and Mg contents are not at the lower limit, respectively, the strength is insufficient. In the case of the alloy 30 A, since the Si content exceeds the upper limit 粗, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloy 32A, since the Mg content exceeds the upper limit, the Mg effect is saturated and the economy is poor. In the case of the alloys 27A to 32A, the appearance of the cross section after the treatment of the aluminum oxide film did not occur unevenly. (About the hot rolled material) As shown in Table 8, in the case of the alloys 29 A and 3 1A, since the Si and Mg contents respectively did not reach the lower limit, the strength was insufficient. In the case of the alloy 30 A, since the Si content exceeds the upper limit 粗, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of Alloy 32A, since the Mg content exceeds the upper limit, the Mg effect is saturated and the economy is poor. In the case of the alloy 2 7 A to 3 2 A, an unevenness occurs in the appearance of the cross section after the treatment of the aluminum oxide film. (5) Fifth Embodiment This embodiment relates to the fourth invention. The aluminum alloy used in the present embodiment is a 7000-series Al-Zn-Mg-based alloy. Alloys 33A and 34A shown in Table 9 were used as the alloys of the examples, and alloys 35A to 38A were used as the alloys of the comparative examples. -60- 200900512 [Table 9] Distinguishing number element (% by mass) Alloy type preparation Mg Si Fe Cu Μη Cr Zn Ti Zr Morning alloy gold alloy 33A 2.5 0.1 0.2 1.8 - 0.2 5.5 0.02 - 7000 Alloy 34A 3.5 0.2 0.2 2.0 - - 8.5 0.02 0.2 7000 series ratio I alloy 35A 0.3 0.1 0.2 2.2 - 0.1 4.0 0.02 - 7000 series Mg not lower limit 値 alloy 36A 5.0 0.2 0.2 2.0 - 0.1 5.0 0.02 - 7000 Series Mg exceeds the limit alloy 37A 2.5 0.1 0.2 2.2 - 0.1 2.4 0.02 - 7000 Zn not lower limit 値 alloy 38A 3.0 0.2 0.2 2.0 - 0.1 9.5 0.02 - 7000 Zn exceeds the upper limit 处理 (treatment) First, the alloys 33A to 38A are sequentially passed through the melting step and the dehydrogenation step In the filtration step and the casting step, an ingot having a thickness of 500 mm was produced. Next, a cut material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by heat-treating the ingot described above and then hot rolling. Both the cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. That is, the above cut material was kept at 500 ° C for 4 hours. Further, the obtained cut material and hot rolled material were melted at 470 ° C, and then subjected to aging treatment at 110 ° C for 48 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the fourth invention, and the hot rolled material after the above treatment is not. Further, only the cutting material using the alloys 33 A and 34A belongs to the embodiment of the fourth invention. Next, for the cut material and the hot rolled material after the above treatment, a strong -61 - 200900512 degree test and an aluminum oxide film treatability evaluation test were performed. The method and evaluation criteria of each test were the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the strength evaluation criteria are as follows. In other words, in terms of strength, the tensile strength of 2 50 N/mm 2 or more was judged as pass (〇), and the tensile strength of less than 2500 N/mm 2 was judged as unacceptable (X ). The test results are shown in Table 1. [Table 1〇]

區分 編號 強度 氧化鋁膜處理後外觀 拉伸強度 (N/mm2) 安全限應力 (N/mm2) 判定 表面外觀 截面外觀 切 割 材 實 施 例 合金33A 425 364 〇 〇 〇 合金34A 513 450 〇 〇 〇 比 較 例 合金35A 198 167 X 〇 〇 合金36A 289 189 〇 X 〇 合金37A 210 132 X 〇 〇 合金38A 605 526 〇 X 〇 熱 壓 延 材 比 較 例 合金33A 442 380 〇 〇 X 合金34A 535 474 〇 〇 X 合金35A 212 174 X 〇 X 合金36A 305 203 〇 X X 合金37A 227 148 X 〇 X 合金38A 616 536 〇 X X (關於切割材） 如表1 0所示，在合金3 5 A、3 7 A的情形，由於Mg、Distinguishing the strength of the aluminum alloy film after treatment. Tensile strength (N/mm2) Safety limit stress (N/mm2) Judging surface appearance Cross-section appearance Cutting material Example alloy 33A 425 364 Niobium alloy 34A 513 450 〇〇〇Comparative example Alloy 35A 198 167 X 〇〇 alloy 36A 289 189 〇X 〇 alloy 37A 210 132 X 〇〇 alloy 38A 605 526 〇X 〇 hot rolled material comparative example alloy 33A 442 380 〇〇X alloy 34A 535 474 〇〇X alloy 35A 212 174 X 〇X Alloy 36A 305 203 〇XX Alloy 37A 227 148 X 〇X Alloy 38A 616 536 〇XX (About cutting material) As shown in Table 10, in the case of alloys 3 5 A, 3 7 A, due to Mg ,

Zn含量分別未達下限値，強度不足。在合金36A、38A的 -62- 200900512 情形，由於Mg、Zn含量分別超過上限値，氧化鋁膜處理 後的表面外觀發生不均勻。在合金33A〜38A的情形，在 氧化鋁膜處理後的截面外觀不會發生不均勻。 (關於熱壓延材） 如表1 〇所示，在合金3 5 A、3 7 A的情形，由於M g、The Zn content is less than the lower limit and the strength is insufficient. In the case of -62-200900512 of the alloys 36A, 38A, since the Mg and Zn contents respectively exceed the upper limit 値, the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloys 33A to 38A, the cross-sectional appearance after the treatment of the aluminum oxide film did not occur unevenly. (About hot rolled material) As shown in Table 1 ,, in the case of alloys 3 5 A, 3 7 A, due to Mg,

Zn含量分別未達下限値，強度不足。在合金36A、38A的 情形，由於Mg、Zn含量分別超過上限値，氧化鋁膜處理 後的表面外觀發生不均勻。在合金33 A〜3 8A的情形，在 氧化鋁膜處理後的截面外觀會發生不均勻。 (6 )第6實施例 本實施例是關於第5發明。本實施例使用的鋁合金， 是5000系的Al-Mg系合金。 使用表11所示的合金1B〜12B作爲實施例合金，使 用合金13B〜22B作爲比較例合金。 -63- 200900512 ητThe Zn content is less than the lower limit and the strength is insufficient. In the case of the alloys 36A and 38A, since the Mg and Zn contents respectively exceed the upper limit 値, the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloys 33 A to 3 8A, the cross-sectional appearance after the treatment of the aluminum oxide film may be uneven. (6) Sixth Embodiment This embodiment relates to the fifth invention. The aluminum alloy used in the present embodiment is a 5000-series Al-Mg-based alloy. Alloys 1B to 12B shown in Table 11 were used as the alloys of the examples, and alloys 13B to 22B were used as the alloys of the comparative examples. -63- 200900512 ητ

1 1 JIS5052 合金 JIS5083 合金 Mg未達下限値 iM m Si超過上限値 Fe超過上限値 Cu超過上限値 Μη超過上限値 Cr超過上限値 Zn超過上限値 Ti超過上限値 Zr超過上限値 合金 種類 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 元素(質量％) Ν 1 ! i i—Η ί 1 i 1 ι—Η 1 1 1 1 1 1 1 1 1 1 1 1 寸 〇 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 J 0.01 | 0.01 0.01 | 0.01 0.01 0.01 0.01 0.01 0.01 0.15 0.01 C3 N 1 1 1 i 1 1 1 1 1 m ο 1 1 1 1 1 1 1 1 1 c5 1 1 1 1 1 1 1 1 1 0.05 cn Ο 1 0.15 1 1 1 1 1 1 1 &lt;〇· 〇 1 1 1 Μη 1 m d 1 1 1 1 0.05 1 卜 d 0.05 1 Ό d 1 1 1 1 1 (Ν 1 1 1 1 U 1 1 1 1 1 rn 1 1 1 1 1 1 1 1 1 1 卜 〇 1 1 i 1 1 &lt;υ ttH m ο m 〇 m o m 〇 ΓΛ ο in o cn o m ο m ο m ο m ο &lt;N Ο m Ο m 〇 〇 〇 ί—Η m 〇 m ο m ο m ο CO 〇 ΓΟ 〇 y—i Ο 〇 o o ο m O T-H o ι—Η Ο ο Ο r-H Ο Ο 〇 Ο 00 〇 〇 r—Η Ο Ο ο ο 〇 〇 (Ν (N IT) 10.5 in — 寸 in — yr) (Ν cn 1 13.5 寸· in 寸· ^Τ) — iT) 寸 寸· 編號 合金IB 合金2B 合金3B 合金4B 合金5Β 合金6B 合金7B 1 合金8Β 合金9B 合金10B 合金11B 合金12Β 1合金13B I 合金MB 合金15B 合金16B 1合金ΠΒ 合金18Β 合金19B 合金20B 合金21B 合金22B ^ fell Φ 舾習匡4π領 ：Η鎰匡&lt;ίπ領 -64 - 200900512 (處理） 首先，將合金1B〜22B依序經由熔解步驟、脫氫氣步 驟、過濾步驟及鑄造步驟的處理，製作出板厚5 00mm的 鑄塊。 然後，將前述鑄塊經由熱處理步驟進行處理。亦即， 將前述鑄塊以3 5 0 °C保持4小時。 接著，從熱處理後的鑄塊製作出切割材和熱壓延材。 切割材是將前述鑄塊經由切割步驟處理所得。熱壓延材， 是將前述鑄塊進行熱壓延而製得。切割材和熱壓延材都是 厚度20mmx寬度lOOOmmx長度2000mm的鋁合金厚板。 因此，前述處理後的切割材是屬於第5發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金1B〜22B之切割材屬於第5發明的實施 例。 接著’對於前述處理後的切割材及熱壓延材，進行平 坦性試驗、板厚精度評價試驗、強度試驗以及氧化鋁膜處 理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 試驗結果顯不於表12及表13。 -65- 200900512 【(NI s 截面組織 平均結晶粒徑 (// m) 〇 卜 〇 卜 o Ο MO Ο 寸 Ο Ο ί/Ί 〇 in Ο Ο Ο 〇 Ο (Ν 發生鑄造裂痕，無法進行製造 〇 Ο in Ο ί〇 o 寸 〇 Ό Ο Ό 氧化鋁膜處理後外觀 截面外觀 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 表面外觀 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 X X 〇 X X 〇 〇 〇 強度 判定 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 X 〇 〇 〇 〇 〇 〇 〇 〇 安全限應力 (N/mm2) 〇 〇 〇〇 Ό 寸 (Ν 卜 Γ ΟΟ ο 寸 卜 寸 寸 Ό 寸 Ο 寸 T—1 &lt;Ν 卜 (Ν iT) (Ν 卜 VO σ\ 寸 Ο 卜 拉伸強度 (N/mm2) 寸 (N ITi &lt;N &lt;N 00 cn 二 卜 Ο &lt;N v〇 (N (N in 卜 Ο m m oo (N m 卜 CN 00 ο m m 板厚精度 判定 ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ 平坦度 判定 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 (mm/m) 0.25 yn (N 〇 0.28 0.28 ο 0.29 0.26 0.27 0.28 0.29 0.26 0.28 (Ν Ο 0.29 0.30 0.29 0.30 0.29 0.28 0.29 0.28 編號 合金1B 合金2B 合金3B 合金4B 合金5Β 合金6Β 合金7Β 合金8B 合金9B 合金10B 合金11B 合金12B 合金13Β 合金14Β 合金15B 合金16Β 合金17B 合金18B 合金19B 合金20B 合金21Β 合金22Β l5i) Φ 运SS怎 -66- 2009005121 1 JIS5052 alloy JIS5083 alloy Mg less than the lower limit 値iM m Si exceeds the upper limit 値Fe exceeds the upper limit 値Cu exceeds the upper limit 値Μη exceeds the upper limit 値Cr exceeds the upper limit 値Zn exceeds the upper limit 値Ti exceeds the upper limit 値Zr exceeds the upper limit 値 alloy type 5000 series 5000 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series elements (% by mass) Ν 1 ! ii —Η ί 1 i 1 ι—Η 1 1 1 1 1 1 1 1 1 1 1 1 1 inch 〇 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 0.01 1 1 1 i 1 1 1 1 1 m ο 1 1 1 1 1 1 1 1 1 c5 1 1 1 1 1 1 1 1 1 0.05 cn Ο 1 0.15 1 1 1 1 1 1 1 &lt;〇· 〇1 1 1 Μη 1 md 1 1 1 1 0.05 1 卜d 0.05 1 Ό d 1 1 1 1 1 (Ν 1 1 1 1 U 1 1 1 1 1 rn 1 1 1 1 1 1 1 1 1 1 〇 1 1 i 1 1 &lt;υ ttH m ο m 〇mom 〇ΓΛ ο in o cn om ο m ο m ο m ο &lt;N Ο m Ο m 〇〇〇ί—Η m 〇m ο m ο m ο C O 〇ΓΟ — — — — — — — — H H H H H H H H H Η Η Η Η N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N N Yr) (Ν cn 1 13.5 inch · in inch · ^Τ) — iT) inch inch · numbered alloy IB alloy 2B alloy 3B alloy 4B alloy 5Β alloy 6B alloy 7B 1 alloy 8Β alloy 9B alloy 10B alloy 11B alloy 12Β 1 alloy 13B I Alloy MB alloy 15B alloy 16B 1 alloy ΠΒ alloy 18 Β alloy 19B alloy 20B alloy 21B alloy 22B ^ fell Φ 舾 匡 π 4π collar: Η镒匡 &lt; ίπ collar-64 - 200900512 (treatment) First, the alloy 1B~22B Ingots having a thickness of 500 mm were produced through a melting step, a dehydrogenation step, a filtration step, and a casting step. Then, the aforementioned ingot is processed through a heat treatment step. That is, the aforementioned ingot was held at 350 ° C for 4 hours. Next, a cut material and a hot rolled material were produced from the ingot after the heat treatment. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to hot rolling. Both the cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the production method of the fifth invention, and the hot rolled material after the above treatment is not. Further, only the cutting material using the alloys 1B to 22B belongs to the embodiment of the fifth invention. Next, a flatness test, a plate thickness precision evaluation test, a strength test, and an alumina film rationality evaluation test were performed on the cut material and the hot rolled material after the above treatment. The method and evaluation criteria of each test were the same as those in the first embodiment. The test results are not shown in Table 12 and Table 13. -65- 200900512 [(NI s cross-sectional organization average crystal grain size (/ / m) 〇 〇 〇 Ο Ο Ο Ο Ο Ο Ο ί ί Ν Ο Ο Ο Ο 〇Ο Ν (Ν Casting cracks, can not be manufactured 〇 Ο in Ο 〇 〇 〇 氧化铝 氧化铝 Alumina film treated appearance cross-sectional appearance 〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇 surface appearance 〇〇〇〇〇〇〇〇 〇〇〇〇〇XX 〇XX 〇〇〇Strength determination 〇〇〇〇〇〇〇〇〇〇〇〇X 〇〇〇〇〇〇〇〇Safety limit stress (N/mm2) 寸 Inch (Ν IT Γ ο 寸 inch inch inch inch inch inch inch inch T-1 &lt;Ν 卜 (Ν iT) (Ν VO σ Ο 拉伸 拉伸 tensile strength (N / mm2) inch (N ITi &lt; N &lt; N 00 Nn 二Ο Ο N N N N N N N N N N N N N N N N N ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ Flatness determination〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇〇 〇(mm/m) 0.25 yn (N 〇0.28 0.28 ο 0.29 0.26 0.27 0.28 0.29 0.26 0.28 (Ν Ο 0.29 0.30 0.29 0.30 0.29 0.28 0.29 0.28 No. alloy 1B alloy 2B alloy 3B alloy 4B alloy 5 Β alloy 6 Β alloy 7 Β alloy 8B alloy 9B Alloy 10B Alloy 11B Alloy 12B Alloy 13Β Alloy 14Β Alloy 15B Alloy 16Β Alloy 17B Alloy 18B Alloy 19B Alloy 20B Alloy 21Β Alloy 22Β l5i) Φ 运 SS How-66- 200900512

截面組織 平均結晶粒徑 (β m) 160 150 170 140 140 160 160 150 150 160 170 150 210 m 鉍 it 賴 坭 璀 蜮 m 11 粼 170 170 160 130 120 160 160 140 氧化鋁膜處理後外觀 截面外觀 X X X X X X X X X X X X X X X X X X X X X 表面外觀 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 X X 〇 X X 〇 〇 〇 強度 判定 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 X 〇 〇 〇 〇 〇 〇 〇 〇 安全限應力 (N/mm2) 103 108 139 162 197 154 150 151 157 145 126 160 1 里 &lt;3\ 139 139 154 153 150 139 142 150 拉伸強度 (N/mm2) 215 224 293 312 379 3102 295 298 310 I 299 222 303 | 179 I 295 294 302 309 306 290 296 299 板厚精度 判定 ◎ ◎ 〇 〇 〇 ◎ 〇 〇 〇 〇 ◎ 〇 ◎ ◎ 〇 〇 ◎ 〇 〇 〇 〇 平坦度 判定 X X X X X X X X X X X X X X X X X X X X X (mm/m) 0.42 0.43 0.48 0.60 0.71 0.48 0.49 0.48 0.51 0.49 0.42 0.49 0.41 0.49 0.50 0.49 0.49 0.48 0.49 0.50 0.49 編號 合金1B 合金2B 合金3B 合金4B 合金5B 合金6B 合金7B 合金8B 合金9B 合金10B 合金11B 合金12B 合金13B 合金14B 合金15B 合金16B 合金17B 合金18B 合金19B 合金20B 合金21B 合金22B 踔φ ：Η鎰匡 -67- 200900512 表12顯示切割材之試驗結果。表12中，合金1B〜 12B屬於第5發明的實施例，合金13B〜22B屬於比較 例。表1 3顯示熱壓延材的試驗結果。表1 3中，合金1B 〜22B全都屬於比較例。 (關於切割材） 如表12所示，在合金1B〜13B、合金15B〜22B的情 形，加工應變少，彎曲小。亦即平坦度良好。又板厚精度 良好。 在合金14B的情形，由於Mg含量超過上限値’會發 生鑄造裂痕，無法進行製造。在合金1 3 B的情形，由於 Mg含量未達下限値，其強度不足。 在合金1B〜13B、17B、20B〜22B的情形，氧化鋁膜 處理後的表面外觀未發生不均勻。在合金15B、16B、 18B、19B各個的情形，由於Si、Fe、Μη、Cr含量分別超 過上限値，會生成粗大的金屬間化合物，氧化鋁膜處理後 的表面外觀會發生不均勻。在合金1B〜13B、15B〜22B 的情形，氧化鋁膜處理後的表面外觀不會發生不均勻。 又在合金 17B、20B、21B、22B各個的情形，由於 Cn、Zn、Ti、Zr的含量分別超過上限値，其等的效果達 飽和，故經濟性不佳。 (關於熱壓延材） 如表13所示，在合金1B〜13B、15B〜22B的情形， -68- 200900512 會累積加工應變，壓延方向的彎曲大。亦即平坦度不佳。 又板厚精度比起切割材，幾乎都比較差。 在合金14B的情形，由於Mg含量超過上限値，會發 生鑄造裂痕，無法進行製造。在合金13B的情形，由於 Mg含量未達下限値，其強度不足。 在合金15B、16B、18B、19B各個的情形，由於Si、 Fe、Μη、Cr含量分別超過上限値，會生成粗大的金屬間 化合物，氧化鋁膜處理後的表面外觀會發生不均勻。在合 金1B〜13B、15B〜22B的情形，氧化鋁膜處理後的表面 外觀發生不均勻。 (7 )第7實施例 本實施例是關於第5發明。在本實施例，是使用表1 1 所示的合金3 B。 (處理） 首先，將合金3 B依序經由熔解步驟、脫氫氣步驟、 過瀘步驟及鑄造步驟的處理，製作出板厚5 00mm的鑄 塊。 接著，將前述鑄塊藉由熱處理步驟進行處理。亦即， 將前述鑄塊用表14所示的條件進行熱處理。 然後，將前述鑄塊藉由切割步驟的處理來獲得切割 材。切割材爲厚度20mmx寬度lOOOmmx長度2000mm的鋁 合金厚板。 -69- 200900512 [表 14] 區分 編號 均質化熱處理 平坦j 度 板厚精度 切削時的切 丨削斷裂性 (mm/m) 判定 判定 (f@/l〇g) 判定 切 割 材 實施例 B1 合金3B 350°Cx2 小時 0.28 〇 ◎ 1030 〇 B2 合金3B 250°Cx4 小時 0.36 〇 ◎ 1140 〇 比較例 B3 合金3B Μ j\w 0,44 X 〇 1290 〇 B4 合金3B 420°Cx4 小時 0.26 〇 ◎ 920 X B5 合金3B 150°Cx2 小時 0.42 X 〇 1230 〇 因此，熱處理條件符合第5發明之B 1及B2，是屬於 第5發明的實施例；熱處理條件不符合第5發明的B3〜 B 5，是屬於比較例。 對於前述處理後的切割材，進行平坦性評價試驗、板 厚精度評價試驗以及切削性評價試驗。 &lt;平坦性評價試驗&gt; 平坦性評價，是測定鑄造方向每1 m的彎曲量（平坦 度），平坦度爲 〇 . 4 m m /1 m長以下的情形判定爲合格 (〇），在超過〇 · 4 m m /1 m長的f青形判定爲不合格（X )。 &lt;板厚精度評價試驗&gt; 關於板厚精度評價試驗’是和第1實施例的情形相 同。 切削性評價試驗 -70- 200900512 切削性（切削斷裂性的評價）是測定’ 鑽孔加工時切屑之每單位質量的個數。具體 徑 5 mm φ的鑽孔器，以旋轉數 7〇〇〇 rpm 300mm /分進行鑽孔加工，測定所產生之每 數。將1 000個/l〇g以上的情形判定爲合格 達1 000個/10g的情形判定爲不合格（X )。 試驗結果顯示於表14。 如表14所示，實施例B1、B2之熱處理 發明，因此平坦度、板厚精度及切削性良好 B3，由於未進行熱處理，其平坦度不良，. Bl、B2，其板厚精度稍差。在比較例B4， 比第5發明的範圍高，比起實施例B1、B2 差。又在比較例B5，由於處理溫度比第‘· 低，其平坦度不良，且比起實施例B 1、B 2 稍差。 (8 )第8實施例 本實施例是關於第6發明，本實施例使 3 000系的Al-Mn系合金。 使用表15所示的合金23B、24B作爲實 用合金25B、：26B作爲比較例合金。 用鑽孔器進行 而言，使用直 及進給速度 10g的切屑個 (〇），將未 條件符合第5 。又在比較例 &amp;比起實施例 由於處理溫度 ，其切削性稍 5發明的範圍 ，其板厚精度 用的鋁合金是 施例合金，使 -71 - 200900512 [表 15] 區分 編號 元素(質量％) 合金 種類 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr 實 施合 例金 合金23B - 0.1 0.3 - 0.5 - - 0.01 - 3000 系 合金24B - 0.1 0.4 ~ 0.9 - - 0.01 - 3000 系 比 fe合 例金 合金25B - 0.1 0.4 — 0.2 - - 0.01 - 3000 系 Μη未達下限値 合金26B - 0.1 0.3 — 1.7 - - 0.01 - 3000 系 Μη超過上限値 (處理） 首先，將合金2 3 B〜2 6 B依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理，製作出板厚5 00mm 的鑄塊。 接著，將前述鑄塊藉由熱處理步驟進行處理。亦即， 將前述鑄塊在3 5 0 °C保持4小時。 接著，從前述熱處理後的鑄塊製作出切割材和熱壓延 材。切割材是將前述鑄塊經由切割步驟處理所得。熱壓延 材，是將前述鑄塊進行熱壓延而製得。切割材和熱壓延材 都是厚度 20mmx寬度 lOOOmmx長度 2000mm的銘合金厚 板。 因此，前述處理後的切割材是屬於第6發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金23 B、24B之切割材屬於第6發明的實施 例。 接著，對於前述處理後的切割材及熱壓延材，進行平 坦性評價試驗、板厚精度評價試驗、強度試驗以及氧化鋁 膜處理性評價試驗。 -72- 200900512 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同’故強度的評價 基準如下。亦即，在強度方面，將拉伸強度90N/mm2以上 的情形判定爲合格（〇)，將拉伸強度未達90N/mm2的情 形判定爲不合格（X )。 試驗結果顯不於表1 6。 -73- 200900512 【91 5 氧化鋁膜處理後外觀 截面外觀 〇 〇 〇 〇 X X X X 表面外觀 〇 〇 〇 X 〇 〇 〇 X 強度 判定 〇 〇 X 〇 〇 〇 〇 〇 安全限應力 (N/mm2) 00 ο m 00 cn 们 Τ—Η 拉伸強度 (N/mm2) σν Ο iTi 00 00 cn 1-^ σν 〇 f—^ 板厚精度 判定 ◎ ◎ ◎ ◎ ◎ 〇 ◎ 〇 平坦度 判定 〇 〇 〇 〇 X X X X (mm/m) 1 m Ο m (Ν ο &lt;Ν &lt;Ν Ο 〇 寸 〇 寸 〇 寸 〇 〇 ! 編號 合金23Β 合金24Β 合金25Β 合金26Β 合金23B 合金24B 合金25Β 合金26B 區分 舾辑掌 ^ fin ^ ^ -74- 200900512 (關於切割材） 如表16所示，在合金23 B〜26B的情形，加工應變 小，彎曲小。亦即平坦度良好，又板厚精度優異。 在合金25B的情形，由於Μη含量未達下限値，強度 不足。在合金26Β的情形，由於Μη含量超過上限値，會 生成粗大的金屬間化合物，氧化鋁膜處理後的表面外觀發 生不均勻。在合金23 Β〜26Β的情形，在氧化鋁膜處理後 的截面外觀不會發生不均勻。 (關於熱壓延材） 如表6所示，在合金23Β〜26Β的情形，會累積加工 應變，壓延方向的彎曲大。亦即平坦度不佳。又板厚精度 比起切割材，幾乎都比較差。 在合金2 5 Β的情形，由於Μη含量未達下限値，比起 其他的熱壓延材，其強度稍差。在合金2 6Β的情形，由於 Μη含量超過上限値，會生成粗大的金屬間化合物，在氧 化鋁膜處理後的表面外觀發生不均勻。在合金23Β〜26Β 的情形，氧化鋁膜處理後的截面外觀發生不均勻。 (9 )第9實施例 本實施例是關於第7發明。本實施例使用的鋁合金是 6000系的Al-Mg-Si系合金。 使用表17所示的合金27B、28B作爲實施例合金，使 用合金29B〜32B作爲比較例合金。 -75- 200900512 表17] 區分 編號 元素(質量％) 合金 種類 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr 實 i合 例金 合金27B 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 6000 系 合金28B 0.5 0.9 0.2 - 0.1 - - 0.02 — 6000 系 比 較合 例金 合金29B 0.9 0.1 0.5 - 0.1 — — 0.02 - 6000 系 Si未達下限値 合金30B 0.9 1.8 0.4 - 0.1 - - 0.02 — 6000 系 Si超渦h限値 合金31B 0.2 0.5 0.5 - 0.1 — 0.02 - 6000 系 Mg未達下限値 合金32B 1.7 0.5 0.4 - 0.1 — 0.02 - 6000 系 Mg超過上限値 (處理） 首先，將合金27B〜32B依序經由熔解步驟、脫氫氣 步驟' 過濾步驟及鑄造步驟的處理，製作出板厚5 00mm 的鑄塊。 接著，將前述鑄塊藉由熱處理步驟進行處理。亦即， 將前述鑄塊在3 5 0 °C保持4小時。 接著，從熱處理後的鑄塊製作出切割材和熱壓延材。 切割材是將前述鑄塊經由切割步驟處理所得。熱壓延材， 是將鑄塊進行熱壓延而製得。切割材和熱壓延材都是厚度 20mmx寬度lOOOmmx長度2000mm的鋁合金厚板。 進一步，將製得的切割材及熱壓延材以5 2 0 °C進行熔 體化處理，然後以1 7 5 °C進行8小時的時效處理。 因此，前述處理後的切割材是屬於第7發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金27B、2 8B之切割材屬於第7發明的實施 例。 接著，對於前述處理後的切割材及熱壓延材，進行強 -76- 200900512 度試驗以及氧化鋁膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度200N/mm2以 上的情形判定爲合格（〇），將拉伸強度未達200N/mm2 的情形判定爲不合格（X )。 試驗結果顯示於表1 8。 [表 18]Cross-sectional structure average crystal grain size (β m) 160 150 170 140 140 160 160 150 150 160 170 150 210 m 铋it 坭璀蜮 坭璀蜮 m 11 粼 170 170 160 130 120 160 160 140 Alumina film treated appearance cross-sectional appearance XXXXXXXXXXXXXXXXXXXXX Surface appearance 〇〇〇〇〇〇〇〇〇〇〇〇〇 XX 〇 XX 〇〇〇 Strength determination 〇〇〇〇〇〇〇〇〇〇〇〇 X 〇〇〇〇〇〇〇〇 Safety limit stress (N/ Mm2) 103 108 139 162 197 154 150 151 157 145 126 160 1 Lane &lt;3\ 139 139 154 153 150 139 142 150 Tensile strength (N/mm2) 215 224 293 312 379 3102 295 298 310 I 299 222 303 | 179 I 295 294 302 309 306 290 296 299 Determination of plate thickness accuracy ◎ ◎ 〇〇〇 ◎ 〇〇〇〇 ◎ 〇 ◎ ◎ 〇〇 ◎ 〇〇〇〇 flatness judgment XXXXXXXXXXXXXXXXXXXXX (mm/m) 0.42 0.43 0.48 0.60 0.71 0.48 0.49 0.48 0.51 0.49 0.42 0.49 0.41 0.49 0.50 0.49 0.49 0.48 0.49 0.50 0.49 No. Alloy 1B Alloy 2B Alloy 3B Alloy 4B Alloy 5B Alloy 6B Alloy 7B Alloy 8B Alloy 9B Alloy 10B Alloy 11B Alloy 12B Alloy 13B Alloy 14B Alloy 15B Alloy 16B Alloy 17B Alloy 18B Alloy 19B Alloy 20B Alloy 21B Alloy 22B 踔 φ : Η镒匡-67- 200900512 Table 12 shows the test results of the cut material . In Table 12, the alloys 1B to 12B belong to the embodiment of the fifth invention, and the alloys 13B to 22B belong to the comparative example. Table 1 3 shows the test results of the hot rolled steel. In Table 1 3, Alloys 1B to 22B are all comparative examples. (About the cutting material) As shown in Table 12, in the case of the alloys 1B to 13B and the alloys 15B to 22B, the processing strain was small and the bending was small. That is, the flatness is good. The plate thickness accuracy is good. In the case of the alloy 14B, since the Mg content exceeds the upper limit 値', a casting crack occurs and manufacturing cannot be performed. In the case of the alloy 1 3 B, since the Mg content is less than the lower limit 値, the strength is insufficient. In the case of the alloys 1B to 13B, 17B, and 20B to 22B, the surface appearance after the treatment of the aluminum oxide film did not occur unevenly. In the case of each of the alloys 15B, 16B, 18B, and 19B, since the Si, Fe, Μ, and Cr contents exceed the upper limit 分别, coarse intermetallic compounds are formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloys 1B to 13B and 15B to 22B, the surface appearance after the treatment of the aluminum oxide film did not occur unevenly. Further, in the case of each of the alloys 17B, 20B, 21B, and 22B, since the contents of Cn, Zn, Ti, and Zr exceed the upper limit 値, the effects thereof are saturated, and the economy is not good. (Regarding hot rolled material) As shown in Table 13, in the case of the alloys 1B to 13B and 15B to 22B, -68-200900512 accumulated machining strain, and the bending in the rolling direction was large. That is, the flatness is not good. The plate thickness accuracy is almost inferior to that of the cutting material. In the case of the alloy 14B, since the Mg content exceeds the upper limit 铸造, casting cracks occur and manufacturing cannot be performed. In the case of the alloy 13B, since the Mg content is less than the lower limit, the strength is insufficient. In the case of each of the alloys 15B, 16B, 18B, and 19B, since the Si, Fe, Μ, and Cr contents respectively exceed the upper limit 値, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloys 1B to 13B and 15B to 22B, the surface appearance after the treatment of the alumina film was uneven. (7) Seventh Embodiment This embodiment relates to the fifth invention. In the present embodiment, the alloy 3 B shown in Table 1 is used. (Treatment) First, the alloy 3 B was sequentially subjected to a melting step, a dehydrogenation step, a pulverization step, and a casting step to prepare an ingot having a thickness of 500 mm. Next, the ingot is processed by a heat treatment step. That is, the ingot was heat-treated under the conditions shown in Table 14. Then, the foregoing ingot is processed by a cutting step to obtain a cut material. The cutting material was an aluminum alloy thick plate having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. -69- 200900512 [Table 14] Classification No. Homogenization Heat Treatment Flatness j Degree Thickness Accuracy Cutting and rupture fracture (mm/m) Determination judgment (f@/l〇g) Determination of cutting material Example B1 Alloy 3B 350 ° C x 2 hours 0.28 〇 ◎ 1030 〇 B2 Alloy 3B 250 ° C x 4 hours 0.36 〇 ◎ 1140 〇 Comparative Example B3 Alloy 3B Μ j \ w 0,44 X 〇 1290 〇 B4 Alloy 3B 420 ° C x 4 hours 0.26 〇 ◎ 920 X B5 Alloy 3B 150 ° C x 2 hours 0.42 X 〇 1230 〇 Therefore, the heat treatment conditions are in accordance with the B 1 and B 2 of the fifth invention, and are examples of the fifth invention; the heat treatment conditions do not conform to the B3 to B 5 of the fifth invention, and are comparative example. The flatness evaluation test, the thickness evaluation test, and the machinability evaluation test were performed on the cut material after the above treatment. &lt;Flatness evaluation test&gt; The flatness evaluation is a measurement of the amount of bending (flatness) per 1 m in the casting direction, and the flatness is 〇. 4 mm /1 m or less. f· 4 mm /1 m long f green shape is judged as unacceptable (X). &lt;Thickness Accuracy Evaluation Test&gt; The thickness evaluation test is the same as in the first embodiment. Machinability evaluation test -70-200900512 Machinability (evaluation of cutting fracture property) is the number of pieces per unit mass of the chip during the drilling process. A drill having a diameter of 5 mm φ was drilled at a number of revolutions of 7 rpm and 300 mm/min, and each number produced was measured. When the case of 1 000 pieces/l〇g or more was judged to be 1 000 pieces/10g, it was judged as a failure (X). The test results are shown in Table 14. As shown in Table 14, in the heat treatments of Examples B1 and B2, the flatness, the plate thickness precision, and the machinability were good. B3, since the heat treatment was not performed, the flatness was poor, and Bl and B2 were slightly inferior in sheet thickness accuracy. In Comparative Example B4, it was higher than the range of the fifth invention and was inferior to the examples B1 and B2. Further, in Comparative Example B5, since the treatment temperature was lower than the first, the flatness was poor, and it was slightly inferior to those of Examples B1 and B2. (8) Eighth embodiment This embodiment relates to the sixth invention, and in this embodiment, a 3,000-series Al-Mn alloy is used. Alloys 23B and 24B shown in Table 15 were used as practical alloys 25B and 26B as comparative alloys. For the drill, use a chip with a straight feed rate of 10 g (〇), and the unconditional condition is in accordance with the fifth. Further, in the comparative example & compared with the embodiment, the machinability is slightly in the range of the invention, and the aluminum alloy for the plate thickness precision is the alloy of the example, so that -71 - 200900512 [Table 15] distinguishes the numbered elements (quality %) Alloy type preparation Mg Si Fe Cu Μη Cr Zn Ti Zr Implementation of the combined gold alloy 23B - 0.1 0.3 - 0.5 - - 0.01 - 3000 alloy 24B - 0.1 0.4 ~ 0.9 - - 0.01 - 3000 tying fe alloy gold alloy 25B - 0.1 0.4 — 0.2 - - 0.01 - 3000 The system Μη has not reached the lower limit 値 alloy 26B - 0.1 0.3 — 1.7 - - 0.01 - 3000 The system Μ exceeds the upper limit 处理 (treatment) First, the alloy 2 3 B~2 6 B is sequentially An ingot having a thickness of 500 mm was produced through a melting step, a dehydrogenation step, a filtration step, and a casting step. Next, the ingot is processed by a heat treatment step. That is, the ingot was held at 350 ° C for 4 hours. Next, a cut material and a hot rolled material were produced from the ingot after the heat treatment. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to hot rolling. The cutting material and the hot rolled material are both thick alloy plates of thickness 20mm x width lOOOmmx length 2000mm. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the sixth invention, and the hot rolled material after the above treatment is not. Further, only the cut material using the alloys 23 B and 24B belongs to the embodiment of the sixth invention. Next, a flatness evaluation test, a thickness evaluation test, a strength test, and an alumina film treatability evaluation test were performed on the cut material and the hot rolled material after the above treatment. -72- 200900512 The method and evaluation criteria of each test are the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the evaluation criteria for the strength are as follows. In other words, in the case of strength, the case where the tensile strength was 90 N/mm2 or more was judged as pass (〇), and the case where the tensile strength was less than 90 N/mm2 was judged as unacceptable (X). The test results are not shown in Table 16. -73- 200900512 [91 5 Appearance cross-sectional appearance after treatment of alumina film 〇〇〇〇XXXX Surface appearance 〇〇〇X 〇〇〇X Strength determination 〇〇X 〇〇〇〇〇Safety limit stress (N/mm2) 00 ο m 00 cn Τ Τ Η tensile strength (N/mm2) σν Ο iTi 00 00 cn 1-^ σν 〇f—^ Determination of plate thickness accuracy ◎ ◎ ◎ ◎ ◎ 〇 ◎ 〇 flatness determination 〇〇〇〇 XXXX ( Mm/m) 1 m Ο m (Ν ο &lt;Ν &lt;Ν Ο 〇 inch inch inch inch inch! No. Alloy 23Β Alloy 24Β Alloy 25Β Alloy 26Β Alloy 23B Alloy 24B Alloy 25Β Alloy 26B Division 掌 掌 ^ ^ fin ^ ^ -74- 200900512 (About cutting material) As shown in Table 16, in the case of Alloy 23 B to 26B, the processing strain is small and the bending is small, that is, the flatness is good and the plate thickness precision is excellent. In the case of Alloy 25B Since the Μη content does not reach the lower limit 値, the strength is insufficient. In the case of the alloy 26 ,, since the Μη content exceeds the upper limit 値, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. 26Β In the case where the aluminum oxide film is treated, the cross-sectional appearance does not become uneven. (About the hot rolled material) As shown in Table 6, in the case of the alloy 23 Β to 26 ,, the processing strain is accumulated, and the bending in the rolling direction is large. That is, the flatness is not good, and the plate thickness accuracy is almost inferior to that of the cutting material. In the case of the alloy 2 5 Β, since the Μη content does not reach the lower limit 値, the strength is slightly inferior compared to other hot rolled materials. In the case of the alloy 2 6 ,, since the Μη content exceeds the upper limit 値, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloy 23 Β to 26 ,, the cross section after the treatment of the aluminum oxide film (9) Ninth Embodiment The present embodiment relates to the seventh invention. The aluminum alloy used in the present embodiment is a 6000-series Al-Mg-Si alloy. The alloys 27B and 28B shown in Table 17 are used. As the alloy of the example, alloys 29B to 32B were used as the alloys of the comparative examples. -75- 200900512 Table 17] Distinguished number elements (% by mass) Alloy type Preparation Mg Si Fe Cu Μη Cr Zn Ti Zr 实合合金合金27B 0.9 0.5 0 .5 0.3 0.1 0.2 0.2 0.02 - 6000 Alloy 28B 0.5 0.9 0.2 - 0.1 - - 0.02 — 6000 Comparison of the combined gold alloy 29B 0.9 0.1 0.5 - 0.1 — — 0.02 - 6000 Si is not reached the lower limit 値 alloy 30B 0.9 1.8 0.4 - 0.1 - - 0.02 - 6000 Series Si super vortex h limited alloy 31B 0.2 0.5 0.5 - 0.1 — 0.02 - 6000 Series Mg not reached the lower limit 値 alloy 32B 1.7 0.5 0.4 - 0.1 — 0.02 - 6000 Series Mg exceeds the upper limit 处理 (treatment) First, the alloys 27B to 32B were sequentially subjected to a melting step, a dehydrogenation step, a filtration step, and a casting step to produce an ingot having a thickness of 500 mm. Next, the ingot is processed by a heat treatment step. That is, the ingot was held at 350 ° C for 4 hours. Next, a cut material and a hot rolled material were produced from the ingot after the heat treatment. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to hot calendering. Both the cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 100 mm and a length of 2000 mm. Further, the obtained cut material and hot rolled material were melted at 520 ° C, and then aged at 175 ° C for 8 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the seventh invention, and the hot rolled material after the above treatment is not. Further, only the cut materials using the alloys 27B and 28B belong to the embodiment of the seventh invention. Next, the cut-off material and the hot-rolled material after the above treatment were subjected to a strong-76-200900512 degree test and an aluminum oxide film treatability evaluation test. The method and evaluation criteria of each test were the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the strength evaluation criteria are as follows. In other words, in terms of strength, the tensile strength of 200 N/mm2 or more was judged as pass (〇), and the tensile strength of less than 200 N/mm2 was judged as unacceptable (X). The test results are shown in Table 18. [Table 18]

區分 編號 強度 氧化鋁膜處理後外觀 拉伸強度 (N/mm2) 安全限應力 (N/mm2) 判定 表面外觀 截面外觀 實 合金27B 320 272 〇 〇 〇 切 Μ 例 合金28B 295 251 〇 〇 〇 比 合金29B 112 65 X 〇 〇 割 材 較 合金30B 339 300 〇 X 〇 例 合金31B 175 122 X 〇 〇 合金32B 212 126 〇 〇 〇 合金27B 346 273 〇 〇 X 熱 比 合金28B 319 274 〇 〇 X 壓 合金29B 135 86 X 〇 X 延 較 合金30B 362 322 〇 X X 材 例 合金31B 198 143 X 〇 X 合金32B 233 145 〇 〇 X (關於切割材） 如表18所示，在合金29B、31B的情形，由於Si、Distinguishing between the strength of the number of strength aluminum oxide film after treatment (N/mm2) Safety limit stress (N/mm2) Judging the appearance of the surface appearance of the solid alloy 27B 320 272 〇〇〇 Μ Μ Example alloy 28B 295 251 〇〇〇 ratio alloy 29B 112 65 X 〇〇Cutting material compared to alloy 30B 339 300 〇X 合金Example alloy 31B 175 122 X 〇〇 alloy 32B 212 126 〇〇〇 alloy 27B 346 273 〇〇X heat ratio alloy 28B 319 274 〇〇X pressure alloy 29B 135 86 X 〇X extension alloy 30B 362 322 〇 XX material alloy 31B 198 143 X 〇X alloy 32B 233 145 〇〇X (on the cutting material) As shown in Table 18, in the case of alloys 29B, 31B, due to Si ,

Mg含量分別未達下限値，強度不足。在合金3 0B的情 -77- 200900512 形，由於Si含量超過上限値，會生成粗大的金屬間 物，氧化鋁膜處理後的表面外觀發生不均勻。在合金 的情形，由於Mg含量超過上限値，Mg效果達飽和， 性差。在合金27B〜3 2B的情形，在氧化鋁膜處理後 面外觀不會發生不均句。 (關於熱壓延材） 如表1 8所示，在合金29B、3 1 B的情形，由於 Mg含量分別未達下限値，強度不足。在合金30B 形，由於Si含量超過上限値，會生成粗大的金屬間 物，氧化鋁膜處理後的表面外觀發生不均勻。在合金 的情形，由於Mg含量超過上限値，Mg效果達飽和， 性差。在合金27B〜3 2B的情形，在氧化鋁膜處理後 面外觀會發生不均勻。 (1 0 )第1 0實施例 本實施例是關於第8發明。本實施例使用的鋁合 是7000系的Al-Zn-Mg系合金。 使用表19所示的合金33B、34B作爲實施例合金 用合金35B〜38B作爲比較例合金。 化合 3 2B 經濟 的截The Mg content is less than the lower limit and the strength is insufficient. In the case of the alloy 3 0B -77-200900512, since the Si content exceeds the upper limit 粗, a coarse intermetallic substance is formed, and the surface appearance after the treatment of the alumite film is uneven. In the case of the alloy, since the Mg content exceeds the upper limit M, the Mg effect is saturated and the properties are poor. In the case of the alloys 27B to 3 2B, an unevenness does not occur in the appearance of the aluminum oxide film after the treatment. (About the hot rolled material) As shown in Table 18, in the case of the alloys 29B and 3 1 B, since the Mg content did not reach the lower limit 値, the strength was insufficient. In the alloy 30B shape, since the Si content exceeds the upper limit 粗, a coarse intermetallic substance is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloy, since the Mg content exceeds the upper limit M, the Mg effect is saturated and the properties are poor. In the case of the alloys 27B to 3 2B, uneven appearance occurs after the treatment of the aluminum oxide film. (10) The tenth embodiment This embodiment relates to the eighth invention. The aluminum alloy used in the present embodiment is a 7000 series Al-Zn-Mg alloy. Alloys 33B and 34B shown in Table 19 were used as alloys of the example alloys 35B to 38B as comparative examples. Combination of 3 2B economy

Si、 的情 化合 32B 經濟 的截 金， ，使 -78- 200900512 m i9] 區分 編號 元素(質量％) 合金種 類 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr Έ\ 涵合 合金33B 2.5 0.1 0.2 1.8 - 0.2 4.0 0.02 - 7000 系 /Jlii 口 例金 合金34B 3.5 0.2 0.2 2.0 - - 8.0 0.02 0.2 7000 系 比 例 合 S 合金35B 0.3 0.1 0.2 2.2 一 0.1 4.0 0.02 一 7000 系 Mg未達下限値 合金36B 5.0 0.2 0.2 2.0 - 0.1 5.0 0.02 - 7000 系 Mg超過上限値 合金37B 2.5 0.1 0.2 2.2 0.1 2.4 0.02 - 7000 系 Zn未達下限値 合金38B 3.0 0.2 0.2 2.0 - 0.1 9.5 0.02 - 7000 系 Zn超過上限値 (處理） 首先，將合金33B〜38B依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理，製作出板厚500mm 的禱塊。 接著，將前述鑄塊藉由熱處理步驟進行處理。亦即， 將前述鑄塊在3 0 0 °C保持4小時。 接著，從熱處理後的鑄塊製作出切割材和熱壓延材。 切割材是將鑄塊經由切割步驟處理所得。熱壓延材，是將 前述鑄塊進行熱壓延而製得。切割材和熱壓延材都是厚度 20mmx寬度lOOOmmx長度2000mm的銘合金厚板。 進一步’將製得的切割材及熱壓延材以470°C進行熔 體化處理’然後以1 2 0 °C進行4 8小時的時效處理。 因此’前述處理後的切割材是屬於第8發明的製造方 法所製得之鋁合金厚板，前述處理後的熱壓延材則不是。 又只有使用合金33B、3 4B之切割材屬於第8發明的實施 例。 接著’對於前述處理後的切割材及熱壓延材，進行強 -79- 200900512 度試驗以及氧化鋁膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度2 5 0N/mm2以 上的情形判定爲合格（〇），將拉伸強度未達2 5 0N/mm2 的情形判定爲不合格（X )。 試驗結果顯不於表2 0。 [表 20]Si, the combination of the 32B economic cut-off gold, so that -78- 200900512 m i9] distinguish the number element (% by mass) alloy type preparation Mg Si Fe Cu Μη Cr Zn Ti Zr Έ \ fused alloy 33B 2.5 0.1 0.2 1.8 - 0.2 4.0 0.02 - 7000 series / Jlii mouth gold alloy 34B 3.5 0.2 0.2 2.0 - - 8.0 0.02 0.2 7000 series ratio S alloy 35B 0.3 0.1 0.2 2.2 a 0.1 4.0 0.02 a 7000 series Mg not lower limit 値 alloy 36B 5.0 0.2 0.2 2.0 - 0.1 5.0 0.02 - 7000 Series Mg exceeds the upper limit 値 alloy 37B 2.5 0.1 0.2 2.2 0.1 2.4 0.02 - 7000 Zn is not up to the lower limit 値 alloy 38B 3.0 0.2 0.2 2.0 - 0.1 9.5 0.02 - 7000 Zn exceeds the upper limit 处理 (treatment) First, The alloys 33B to 38B were sequentially subjected to a melting step, a dehydrogenation step, a filtration step, and a casting step to prepare a prayer piece having a thickness of 500 mm. Next, the ingot is processed by a heat treatment step. That is, the ingot was held at 300 ° C for 4 hours. Next, a cut material and a hot rolled material were produced from the ingot after the heat treatment. The cutting material is obtained by treating the ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to hot rolling. Both the cutting material and the hot rolled material are thick alloy plates of thickness 20mm x width 1000mm length 2000mm. Further, the obtained cut material and hot rolled material were melted at 470 ° C and then subjected to aging treatment at 110 ° C for 48 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the eighth invention, and the hot rolled material after the above treatment is not. Further, only the cut material using the alloys 33B and 34B belongs to the embodiment of the eighth invention. Next, the strong-79-200900512 degree test and the aluminum oxide film handleability evaluation test were performed on the cut material and the hot rolled material after the above treatment. The method and evaluation criteria of each test were the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the strength evaluation criteria are as follows. In other words, in terms of strength, the tensile strength of 2500 N/mm2 or more was judged as pass (〇), and the tensile strength of less than 2500 N/mm2 was judged as unacceptable (X). The test results are not as shown in Table 20. [Table 20]

區分 編號 強度 氧化鋁膜處理後外觀 拉伸強度 (N/mm2) 安全限應力 (N/mm2) 判定 表面外觀 截面外觀 實 合金33B 422 363 〇 〇 〇 切 施 例 合金34B 510 449 〇 〇 〇 比 合金35B 193 165 X 〇 〇 割 材 較 mr 合金36B 287 188 〇 X 〇 合金37B 209 130 X 〇 〇 例 合金38B 602 525 〇 X 〇 合金33B 441 380 〇 〇 X 熱 比 合金34B 533 472 〇 〇 X 壓 合金35B 210 172 X 〇 X 延 較 /rtr 合金36B 303 202 〇 X X 材 例 合金37B 224 146 X 〇 X 合金38B 614 535 〇 X X (關於切割材） 如表2 0所示，在合金3 5 B、3 7 B的情形，由於M g、Distinguishing between the strength of the number of strength alumina film after treatment (N/mm2) Safety limit stress (N/mm2) Judging the appearance of the surface appearance of the solid alloy 33B 422 363 Chopping application alloy 34B 510 449 〇〇〇 ratio alloy 35B 193 165 X cutting material compared to mr alloy 36B 287 188 〇X 〇 alloy 37B 209 130 X 〇〇 example alloy 38B 602 525 〇X 〇 alloy 33B 441 380 〇〇X heat ratio alloy 34B 533 472 〇〇X pressure alloy 35B 210 172 X 〇X extension /rtr alloy 36B 303 202 〇XX material alloy 37B 224 146 X 〇X alloy 38B 614 535 〇 XX (on the cutting material) as shown in Table 2 0, in the alloy 3 5 B, 3 7 B case, due to MG,

Zn含量分別未達下限値，強度不足。在合金36B、38B的 -80- 200900512 情形，由於Mg、Zn含量分別超過上限値’氧化鋁膜處理 後的表面外觀發生不均勻。在合金3 3B〜3 SB的情形，在 氧化鋁膜處理後的截面外觀不會發生不均勻。 (關於熱壓延材） 如表2 0所示，在合金3 5 B、3 7 B的情形，由於M g、 Zn含量分別未達下限値，強度不足。在合金36B、38B的 情形，由於Mg、Zn含量分別超過上限値，氧化鋁膜處理 後的表面外觀發生不均勻。在合金33B〜3 8B的情形，在 氧化鋁膜處理後的截面外觀會發生不均勻。 (1 1 )第1 1實施例 本實施例是關於第9發明。本實施例使用的鋁合金， 是5000系的Al-Mg系合金。 使用表2 1所示的合金1 C〜1 2C作爲實施例合金，使 用合金13C〜22C作爲比較例合金。 -81 - 200900512The Zn content is less than the lower limit and the strength is insufficient. In the case of -80 to 200900512 of the alloys 36B and 38B, the surface appearance after the treatment of the Mg and Zn contents exceeding the upper limit 値' of the aluminum oxide film was uneven. In the case of the alloy 3 3B to 3 SB, the cross-sectional appearance after the treatment of the aluminum oxide film did not occur unevenly. (About hot rolled material) As shown in Table 20, in the case of the alloys 3 5 B and 3 7 B, since the Mg and Zn contents are not at the lower limit, respectively, the strength is insufficient. In the case of the alloys 36B and 38B, since the Mg and Zn contents respectively exceed the upper limit 値, the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloys 33B to 3 8B, the cross-sectional appearance after the treatment of the aluminum oxide film may be uneven. (1 1) Embodiment 1 This embodiment relates to the ninth invention. The aluminum alloy used in the present embodiment is a 5000-series Al-Mg-based alloy. Alloys 1 C to 1 2C shown in Table 2 1 were used as the alloys of the examples, and alloys 13C to 22C were used as the alloys of the comparative examples. -81 - 200900512

【I(N^J g JIS5052 合金 JIS5083 合金 Mg未達下限値 M Ή 豳 Si超過上限値 Fe超過上限値 Cu超過上限値 Μη超過上限値 Cr超過上限値 1 Ζη超過上限値 Ti超過上限値 Zr超過上限値 崔 i A ? u π [5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 5000 系 15000 系 5000 系 5000 系 5000 系 5000 系 5000 系 元素(質量％) N 1 1 1 ι—Η 1 1 1 1 r—H 1 1 1 1 t 1 1 1 i 1 1 1 寸 〇 0.01 0.01 0.01 0.01 0.01 0.01 i o.oi | 0.01 0.01 0.01 J 0.01 0.01 J 0.01 I o.oi ! 0.01 0.01 0.01 0.01 0.01 0.01 0.15 0.01 1 1 ! I 1 1 1 1 1 cn 1 1 1 1 1 1 1 1 1 in ο 1 1 1 1 1 1 1 1 1 0.05 m o 1 0.15 1 1 1 1 1 1 1 〇 1 1 I a S 1 m Ο 1 1 1 1 0.05 1 卜 o 0.05 1 ο 1 1 ! I 1 (N 1 1 1 1 1 1 1 1 1 m d 1 1 1 1 1 1 1 1 1 1 卜 〇 1 1 1 1 1 m 〇 cn ο cn ο m ο m ο to O cn O m o m o ro 〇 m ο (Ν ο m ο ο m 〇 〇 m 〇 ο cn 〇 m ο m 〇 m 〇 'χΆ F—Η ο Τ—Η Ο Ο ο r-H Ο m O o o r-H o o Ο Η ο η d τ-Η Ο 00 〇 〇 〇 Η d Ο Ο 〇 Ο iTi ri i/Ί (Ν 卜 in 卜^ 10.4 1 卜 Γ-； 卜 r- 寸· — 心 (Ν 卜 13.0 r-； 卜 寸 〇 Tt- Γ^； — ο — Γ-； 卜 卜 編號 合金1C 合金2C 合金3C 合金4C 合金5C 合金6C 合金7C 合金8C 合金9C 合金IOC 合金lie 合金12C 合金13C 合金14C 合金15C 合金16C 合金17C 合金18C 合金19C 合金20C 合金21C 合金22C 區分 { K習ί %&lt; M λλ 1 篆&lt; π 4 -82- 200900512 (處理） 首先，將合金1C〜22C依序經由熔解步驟、脫氫氣步 驟、過濾步驟及鑄造步驟的處理’製作出板厚5 0 0 m m的 鑄塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割材 是將前述鑄塊經由切割步驟處理所得。熱壓延材，是將前 述鑄塊經由熱處理後進行熱壓延而製得。切割材和熱壓延 材都是厚度20mmx寬度lOOOmmx長度2000mm的鋁合金厚 板。 然後，將前述鑄塊經由熱處理步驟進行處理。亦即， 將前述鑄塊以3 50°C保持4小時。 因此，前述處理後的切割材是屬於第9發明的製造方 法所製得之鋁合金厚板’前述處理後的熱壓延材則不是。 又只有使用合金1C〜22C之切割材屬於第9發明的實施 例。 接著’對於前述處理後的切割材及熱壓延材，進行平 坦性試驗、板厚精度評價試驗、強度試驗以及氧化鋁膜處 理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 又由於厚板的結晶粒徑會影響氧化鋁膜處理性，故和 第1實施例的情形同樣的求出厚板的平均結晶粒徑 試驗結果顯示於表22及表23。 -83 - 200900512 繼II晅礙 ?5-ϋ[I(N^J g JIS5052 alloy JIS5083 alloy Mg not reached the lower limit 値M Ή 豳Si exceeds the upper limit 値Fe exceeds the upper limit 値Cu exceeds the upper limit 値Μη exceeds the upper limit 値Cr exceeds the upper limit 値1 Ζη exceeds the upper limit 値Ti exceeds the upper limit 値Zr exceeds Upper limit 値崔i A ? u π [5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 5000 series 15000 series 5000 series 5000 series 5000 series 5000 Department 5000 element (% by mass) N 1 1 1 ι—Η 1 1 1 1 r—H 1 1 1 1 t 1 1 1 i 1 1 1 inch 〇0.01 0.01 0.01 0.01 0.01 0.01 i o.oi | 0.01 0.01 0.01 J 0.01 0.01 J 0.01 I o.oi ! 0.01 0.01 0.01 0.01 0.01 0.01 0.15 0.01 1 1 ! I 1 1 1 1 1 cn 1 1 1 1 1 1 1 1 1 in ο 1 1 1 1 1 1 1 1 1 0.05 mo 1 0.15 1 1 1 1 1 1 1 〇1 1 I a S 1 m Ο 1 1 1 1 0.05 1 卜 o 0.05 1 ο 1 1 ! I 1 (N 1 1 1 1 1 1 1 1 1 md 1 1 1 1 1 1 1 1 1 1 〇 〇 1 1 1 1 1 m 〇cn ο cn ο m ο m ο to O cn O momo ro 〇m ο (Ν ο m ο ο m 〇〇m 〇ο cn 〇m ο m 〇 m 〇'χΆ F —Η Τ Τ Η O Ο ο r Ο O O O O η τ τ O 00 00 η η Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti Ti 10. 10. 10. 10. 10. 10. -;r-inch--heart (Ν13.0 r-; 卜寸〇Tt- Γ^; — ο — Γ-; Bub number alloy 1C alloy 2C alloy 3C alloy 4C alloy 5C alloy 6C alloy 7C alloy 8C alloy 9C alloy IOC alloy lie alloy 12C alloy 13C alloy 14C alloy 15C alloy 16C alloy 17C alloy 18C alloy 19C alloy 20C alloy 21C alloy 22C distinction { K 习ί % &lt; M λλ 1 篆 &lt; π 4 -82- 200900512 (treatment) First, the alloys 1C to 22C were sequentially subjected to a melting step, a dehydrogenation step, a filtration step, and a casting step to prepare an ingot having a thickness of 500 mm. Next, a cut material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to heat rolling after heat treatment. Both the cutting material and the hot rolled material are aluminum alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Then, the aforementioned ingot is processed through a heat treatment step. That is, the aforementioned ingot was held at 3 50 ° C for 4 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the production method of the ninth invention. The hot rolled material after the above treatment is not. Further, only the cutting material using the alloys 1C to 22C belongs to the embodiment of the ninth invention. Next, a flatness test, a plate thickness precision evaluation test, a strength test, and an alumina film rationality evaluation test were performed on the cut material and the hot rolled material after the above treatment. The method and evaluation criteria of each test were the same as those in the first embodiment. Further, since the crystal grain size of the thick plate affects the handleability of the alumina film, the average crystal grain size of the thick plate was determined in the same manner as in the first example. The test results are shown in Table 22 and Table 23. -83 - 200900512 Following II ? ? ? 5-ϋ

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Z.S ιηΓΟ 9S0 卜ro 8Γ0 sro ΖΓ0 寸Γ0 卜s 8S 卜sz.(NI_o 8S 8S 02 8Γ0 00 υΙ 領&lt;π υ(Ν&lt;^&lt;π οε¥&lt;π U寸^&lt;π 3¾^ 09領&lt;0 υΔ領4Π U8 領&lt;π uol領如 UI»—&lt;領啦 υίΝΙ 領&lt;0 0^領如 υιΙ(ΝΙ^ι&lt;πι υιοζ領如 UI61領啦 0181領如 UIZ.I 領仞 UI91領如 UISI領啦 UI寸一彻啦 CN 區分 fc辑莩 ：H鎰窣 -84- 200900512 截面組織 平均結晶粒徑 (#m) § 140 Ο 寸 r-H 140 o § 140 200 發生鑄造裂痕，無法進行製造 § 〇 150 氧化鋁膜處理後外觀 截面外觀 X X X X X X X X X X X X X X X X X X X X X 表面外觀 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 X X 〇 X X 〇 〇 〇 強度 判定 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 X 〇 〇 〇 〇 〇 〇 〇 〇 安全限應力 (N/mm2) 1—Η 〇 —丨Η 寸 200 in T—H as Η &lt;N i i VO r-H Ο] in \〇 CN IT) 1 * Η 144 (Ν 1—Η 拉伸強度 (N/mm2) 218 227 297 314 383 304 298 297 m cn 303 225 306 r-^ 00 299 298 307 1 312 I 310 295 299 303 板厚精度 判定 ◎ ◎ 〇 〇 〇 ◎ 〇 〇 〇 〇 ◎ 〇 ◎ ◎ 〇 〇 ◎ 〇 〇 〇 〇 Μ 判定 X X X X X X X X X X X X X X X X X X X X X 平坦J (mm/m) 0.43 0.44 0.48 0.61 0.70 0.48 0.48 0.48 0.52 0.50 0.43 0.49 0.42 0.50 0.49 0.49 0.49 0.49 0.49 0.50 0.50 編號 合金1C 合金2C 合金3C 合金4C 合金5C 合金6C 1 合金7C I 合金8C I 合金9C I 合金10C 1 合金lie I 合金12C I 1合金13C I i合金14C 1合金15C 1合金16C 1合金17C 1合金18C 1合金19C 1合金20C I合金21C 1合金22C 區分 ΖΊ η 綠I ij ^ -85- 200900512 表2 2顯示切割材之試驗結果。表2 2中，合金1 C〜 12C屬於第9發明的實施例’合金13C〜22C屬於比較 例。表23顯示熱壓延材的試驗結果。表23中，合金1C 〜2 2 C全都屬於比較例。 (關於切割材） 如表22所示，在合金1C〜13C、合金15C〜22C的情 形，加工應變少，彎曲小。亦即平坦度良好。又板厚精度 良好。 在合金1 4 C的情形，由於M g含量超過上限値，會發 生鑄造裂痕，無法進行製造。在合金1 3 C的情形，由於 Mg含量未達下限値，其強度不足。 在合金1C〜13C、17C、20C〜22C的情形，氧化鋁膜 處理後的表面外觀未發生不均句。在合金15C、16C、 1 8 C、1 9 C各個的情形，由於S i ' F e、Μ η、C r含量分別超 過上限値，會生成粗大的金屬間化合物，氧化鋁膜處理後 的表面外觀會發生不均勻。在合金1C〜13C、15C〜22C 的情形，氧化鋁膜處理後的表面外觀不會發生不均勻。 又在合金17C、20C、21C、22C各個的情形，由於 Cu、Zn、Ti、Zr的含量分別超過上限値，其等的效果達 飽和，故經濟性不佳。 (關於熱壓延材） 如表2 3所示，在合金1 C〜1 3 C、1 5 C〜2 2 C的情形， -86- 200900512 會累積加工應變，壓延方向的彎曲大。亦即平坦度不佳。 又板厚精度比起切割材，幾乎都比較差。 在合金MC的情形，由於Mg含量超過上限値，會發 生鑄造裂痕，無法進行製造。在合金1 3 C的情形，由於 Mg含量未達下限値，其強度不足。 在合金15C、16C、18C、19C各個的情形，由於Si、 Fe、Μη、Cr含量分別超過上限値，會生成粗大的金屬間 化合物，氧化鋁膜處理後的表面外觀會發生不均勻。在合 金1C〜13C、15C〜22C的情形，氧化鋁膜處理後的表面 外觀發生不均勻。 (1 2 )第1 2實施例 本實施例是關於第9發明。在本實施例，是使用表21 所示的合金3 C。 (處理） 首先，將合金3 C依序經由熔解步驟、脫氫氣步驟、 過濾步驟及鑄造步驟的處理，製作出板厚500mm的鑄 塊。 然後，將前述鑄塊藉由切割步驟的處理來獲得切割 材。切割材爲厚度20mmx寬度lOOOmmx長度2000mm的杀呂 合金厚板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材用表24所示的條件進行熱處理。 -87- 200900512 [表 24] 區分 編號 均質化熱處理 平坦 度 板厚精度 切削時的切 削斷裂性 (mm/m) 判定 判定 _〇g) 判定 切 割 材 實施例 C1 合金3C 350°Cx2 小時 0.26 〇 ◎ 1040 〇 C2 合金3C 250°Cx4 小時 0.34 〇 ◎ 1170 〇 比較例 C3 合金3C te 0.45 X 〇 1340 〇 C4 合金3C 420°Cx4 小時 0.23 〇 ◎ 950 X C5 合金3C 150°Cx2 小時 0.42 X 〇 1280 〇 因此，熱處理條件符合第9發明之Cl及C2，是屬於 第9發明的實施例；熱處理條件不符合第9發明的^3〜 C 5，是屬於比較例。 對於前述處理後的切割材，進行平坦性評價試驗、中反 厚精度評價試驗以及切削性評價試驗。 &lt;平坦性評價試驗&gt; 平坦性評價，是測定鑄造方向每1 m的彎曲量（平坦 度），平坦度爲〇.4mm/lm長以下的情形判定爲合格 (〇），在超過〇 _ 4mm/1 m長的情形判定爲不合格（x )。 &lt;板厚精度評價試驗&gt; 關於板厚精度評價試驗’是和第1實施例的情形相 同。 &lt;切削性評價試驗 -88- 200900512 關於切削性評價試驗，是和第7實施例的情形相同。 試驗結果顯示於表24。 如表24所示，實施例C 1、C2之熱處理條件符合第9 發明’因此平坦度、板厚精度及切削性良好。又在比較例 C3’由於未進行熱處理，其平坦度不良，且比起實施例 Cl、C2 ’其板厚精度稍差。在比較例C4，由於處理溫度 比第9發明的範圍高，其切削性稍差。又在比較例C5， 由於處理溫度比第9發明的範圍低，其平坦度不良，且比 起實施例Cl、C2，其板厚精度稍差。 (1 3 )第1 3實施例 本實施例是關於第1 〇發明，本實施例使用的鋁合金 是3 000系的Al-Mn系合金。 使用表25所示的合金23C、24C作爲實施例合金，使 用合金25C、26C作爲比較例合金。 [表 25] 區分 編號 元素(質量％) 合金 手麵 備考 Mg Si Fe Cu Μη Cr Zn Ti Zr 實 施合 例金 合金23C - 0.1 0.3 - 0.5 - - 0.01 - 3000 系 合金24C - 0.1 0.4 - 0.9 - - 0.01 - 3000 系 比 硗合 例金 合金25C - 0.1 0.4 — 0.2 - - 0.01 - 3000 系 Μη未達下限値 合金26C - 0.1 0.3 - 1.7 - - 0.01 - 3000 系 Μη超過h限値 (處理） 首先，將合金23C〜26C依序經由熔解步驟、脫氫氣 -89- 200900512 步驟、過濾步驟及鑄造步驟的處理，製作出板厚5 0 0mm 的禱塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割材 是將前述鑄塊經由切割步驟處理所得。熱壓延材，是將前 述鑄塊經由熱處理後進行熱壓延而製得。切割材和熱壓延 材都是厚度20mmx寬度lOOOmmx長度2000mm的銘合金厚 板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材在3 50°C保持4小時。 因此，前述處理後的切割材是屬於第1 0發明的製造 方法所製得之鋁合金厚板，前述處理後的熱壓延材則不 是。又只有使用合金23C、24C之切割材屬於第10發明的 實施例。 接著’對於前述處理後的切割材及熱壓延材，進行平 坦性評價試驗、板厚精度評價試驗、強度試驗以及氧化鋁 膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度90N/mm2以上 的情形判定爲合格（〇），將拉伸強度未達9〇N/mm2的情 形判定爲不合格（x )。 試驗結果顯示於表2 6。 -90- 200900512 羅s雲i 鼷玫晅镟 〇 d, dZS ιηΓΟ 9S0 卜ro 8Γ0 sro ΖΓ0 inch Γ0 卜s 8S 卜sz.(NI_o 8S 8S 02 8Γ0 00 υΙ collar &lt;π υ(Ν&lt;^&lt;π οε¥&lt;π U inch^&lt;π 33⁄4^ 09 Collar &lt;0 υΔ collar 4Π U8 collar&lt;π uol collar as UI»—&lt;领啦υίΝΙ collar&lt;0 0^领如υιΙ(ΝΙ^ι&lt;πι υιοζ领如 UI61领啦0181领如UIZ.I The collar UI仞 is like the UISI collar UI inch. The CN distinguishes the fc series: H镒窣-84- 200900512 The average crystal grain size of the cross-section (#m) § 140 Ο inch rH 140 o § 140 200 Casting cracks, Unable to manufacture § 〇150 Alumina film treated appearance cross-section appearance XXXXXXXXXXXXXXXXXXXXX Surface appearance 〇〇〇〇〇〇〇〇〇〇〇〇〇XX 〇XX 〇〇〇Strength determination〇〇〇〇〇〇〇〇〇〇〇〇 X 〇〇〇〇〇〇〇〇 Safety limit stress (N/mm2) 1—Η 〇—丨Η inch 200 in T—H as Η &lt;N ii VO rH Ο] in \〇CN IT) 1 * Η 144 (Ν 1—Η Tensile strength (N/mm2) 218 227 297 314 383 304 298 297 m cn 303 225 306 r-^ 0 0 299 298 307 1 312 I 310 295 299 303 Board thickness accuracy judgment ◎ ◎ 〇〇〇 ◎ 〇〇〇〇 ◎ 〇 ◎ ◎ 〇〇 ◎ 〇〇〇〇Μ Judgment XXXXXXXXXXXXXXXXXXXXX Flat J (mm/m) 0.43 0.44 0.48 0.61 0.70 0.48 0.48 0.48 0.52 0.50 0.43 0.49 0.42 0.50 0.49 0.49 0.49 0.49 0.49 0.50 0.50 No. Alloy 1C Alloy 2C Alloy 3C Alloy 4C Alloy 5C Alloy 6C 1 Alloy 7C I Alloy 8C I Alloy 9C I Alloy 10C 1 Alloy lie I Alloy 12C I 1 Alloy 13C I i alloy 14C 1 alloy 15C 1 alloy 16C 1 alloy 17C 1 alloy 18C 1 alloy 19C 1 alloy 20C I alloy 21C 1 alloy 22C classification ΖΊ η green I ij ^ -85- 200900512 Table 2 2 shows the test results of the cutting material . In Table 2, the alloys 1 C to 12C belong to the embodiment of the ninth invention. The alloys 13C to 22C belong to the comparative example. Table 23 shows the test results of the hot rolled product. In Table 23, the alloys 1C to 2 2 C are all comparative examples. (About the cutting material) As shown in Table 22, in the case of the alloys 1C to 13C and the alloys 15C to 22C, the processing strain was small and the bending was small. That is, the flatness is good. The plate thickness accuracy is good. In the case of the alloy 1 4 C, since the Mg content exceeds the upper limit 铸造, casting cracks occur and manufacturing cannot be performed. In the case of the alloy 1 3 C, since the Mg content is less than the lower limit, the strength is insufficient. In the case of the alloys 1C to 13C, 17C, and 20C to 22C, the surface appearance after the treatment of the aluminum oxide film did not cause an unevenness. In the case of alloys 15C, 16C, 1 8 C, and 1 9 C, since the contents of S i ' F e, Μ η, and Cr exceed the upper limit, respectively, coarse intermetallic compounds are formed, and the surface after the treatment of the aluminum oxide film The appearance will be uneven. In the case of the alloys 1C to 13C and 15C to 22C, the surface appearance after the treatment of the aluminum oxide film did not occur unevenly. Further, in the case of each of the alloys 17C, 20C, 21C, and 22C, since the contents of Cu, Zn, Ti, and Zr each exceed the upper limit 値, the effects thereof are saturated, and the economy is not good. (About hot rolled material) As shown in Table 23, in the case of alloys 1 C to 1 3 C and 1 5 C 2 2 C, -86-200900512 accumulates the processing strain, and the bending in the rolling direction is large. That is, the flatness is not good. The plate thickness accuracy is almost inferior to that of the cutting material. In the case of the alloy MC, since the Mg content exceeds the upper limit 铸造, casting cracks occur and manufacturing cannot be performed. In the case of the alloy 1 3 C, since the Mg content is less than the lower limit, the strength is insufficient. In the case of each of the alloys 15C, 16C, 18C, and 19C, since the Si, Fe, Μ, and Cr contents respectively exceed the upper limit 値, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of alloys 1C to 13C and 15C to 22C, the surface appearance after the treatment of the alumina film was uneven. (1 2) Embodiment 1 This embodiment relates to the ninth invention. In the present embodiment, the alloy 3 C shown in Table 21 was used. (Treatment) First, the alloy 3 C was sequentially subjected to a melting step, a dehydrogenation step, a filtration step, and a casting step to prepare a cast piece having a thickness of 500 mm. Then, the foregoing ingot is processed by a cutting step to obtain a cut material. The cutting material was a thick alloy plate having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. Namely, the above-mentioned cut material was heat-treated under the conditions shown in Table 24. -87- 200900512 [Table 24] Classification No. Homogenization Heat Treatment Flatness Thickness Precision Cutting Density (mm/m) at the time of cutting Determination judgment _〇g) Determination of cutting material Example C1 Alloy 3C 350 °C x 2 hours 0.26 〇 ◎ 1040 〇C2 alloy 3C 250°Cx4 hours 0.34 〇◎ 1170 〇Comparative example C3 Alloy 3C te 0.45 X 〇1340 〇C4 Alloy 3C 420°Cx4 hours 0.23 〇◎ 950 X C5 Alloy 3C 150°Cx2 hours 0.42 X 〇1280 〇 The heat treatment conditions are in accordance with the ninth invention, and the heat treatment conditions are not in accordance with the ninth invention, and the heat treatment conditions are not in accordance with the ninth invention. For the cut material after the above treatment, a flatness evaluation test, a medium back thickness evaluation test, and a machinability evaluation test were performed. &lt;Flatness evaluation test&gt; The flatness evaluation is a measurement of the amount of bending (flatness) per 1 m in the casting direction, and the case where the flatness is 〇.4 mm/lm or less is judged as pass (〇), and exceeds 〇_ The case of 4 mm/1 m long was judged as unacceptable (x). &lt;Thickness Accuracy Evaluation Test&gt; The thickness evaluation test is the same as in the first embodiment. &lt;Machinability Evaluation Test -88-200900512 The machinability evaluation test is the same as in the case of the seventh embodiment. The test results are shown in Table 24. As shown in Table 24, the heat treatment conditions of Examples C1 and C2 were in accordance with the ninth invention. Therefore, the flatness, the sheet thickness precision, and the machinability were good. Further, in Comparative Example C3', since the heat treatment was not performed, the flatness was poor, and the plate thickness accuracy was slightly inferior to those of Examples Cl and C2'. In Comparative Example C4, since the treatment temperature was higher than the range of the ninth invention, the machinability was slightly inferior. Further, in Comparative Example C5, since the treatment temperature was lower than the range of the ninth invention, the flatness was poor, and the plate thickness accuracy was slightly inferior to those of the examples C1 and C2. (1 3) The first embodiment is the first invention, and the aluminum alloy used in the embodiment is a 3,000-series Al-Mn alloy. Alloys 23C and 24C shown in Table 25 were used as the alloys of the examples, and alloys 25C and 26C were used as the alloys of the comparative examples. [Table 25] Distinguished number element (% by mass) Alloy hand surface preparation Mg Si Fe Cu Μη Cr Zn Ti Zr Implementation of the joint gold alloy 23C - 0.1 0.3 - 0.5 - - 0.01 - 3000 Alloy 24C - 0.1 0.4 - 0.9 - - 0.01 - 3000 硗 硗 金 金 金 25 25C - 0.1 0.4 — 0.2 - - 0.01 - 3000 Μ 未 未 未 26 26 26 26 26C - 0.1 0.3 - 1.7 - - 0.01 - 3000 Μ 超过 exceeds h limit 处理 (treatment) First, The alloys 23C to 26C were sequentially subjected to a melting step, a dehydrogenation-89-200900512 step, a filtration step, and a casting step to prepare a prayer piece having a thickness of 500 mm. Next, a cut material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to heat rolling after heat treatment. Both the cutting material and the hot rolled material are thick alloy plates with a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. Namely, the above cut material was kept at 3 50 ° C for 4 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the first invention, and the hot rolled material after the above treatment is not. Further, only the cutting material using the alloys 23C and 24C belongs to the embodiment of the tenth invention. Next, a flatness evaluation test, a thickness evaluation test, a strength test, and an alumina film treatability evaluation test were performed on the cut material and the hot rolled material after the above treatment. The method and evaluation criteria of each test were the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the strength evaluation criteria are as follows. That is, in the case of strength, the case where the tensile strength was 90 N/mm2 or more was judged as pass (〇), and the case where the tensile strength was less than 9 〇N/mm2 was judged as unacceptable (x). The test results are shown in Table 26. -90- 200900512 罗斯云i 鼷玫晅镟 〇 d, d

XX

XX

X 〇 〇 〇X 〇 〇 〇

X 〇 Μ锻 (am/M&gt;X 〇 upset (am/M&gt;

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〇 d, w w &quot;W 〇〇 d, w w &quot;W 〇

XX

XX

XX

X i (m/lum) 寸寸Ό 一寸Ό i I寸Ό £s (ΝΙΓ0 (Nls (ΝΙΓ0 議 u9(n領如 區分 _ί習莩 这SS怎 藤涵域怎 -91 - 200900512 (關於切割材） 如表2 6所示，在合金2 3 C〜2 6 C的情形，加工應變 小，彎曲小。亦即平坦度良好，又板厚精度優異。 在合金25C的情形，由於Μη含量未達下限値，強度 不足。在合金26C的情形，由於Μη含量超過上限値，會 生成粗大的金屬間化合物，氧化鋁膜處理後的表面外觀發 生不均勻。在合金23 C〜26C的情形，在氧化鋁膜處理後 的截面外觀不會發生不均勻。 (關於熱壓延材） 如表26所示，在合金23C〜26C的情形，會累積加工 應變，壓延方向的彎曲大。亦即平坦度不佳。又板厚精度 比起切割材，幾乎都比較差。 在合金2 5 C的情形，由於Μη含量未達下限値，比起 其他的熱壓延材，其強度稍差。在合金2 6 C的情形，由於 Μη含量超過上限値，會生成粗大的金屬間化合物，在氧 化鋁膜處理後的表面外觀發生不均勻。在合金23C〜26C 的情形，氧化鋁膜處理後的截面外觀發生不均勻。 (1 4 )第1 4實施例 本實施例是關於第11發明。本實施例使用的鋁合金 是6000系的Al-Mg-Si系合金。 使用表27所示的合金27C、28C作爲實施例合金，使 用合金29C〜32C作爲比較例合金。 -92- 200900512 表27] 區分 編號 元素(質量％) 合金 種類 備考 Mg Si Fe Cu Μη Cr Ζη Ti Zr 實 施合 例金 合金27C 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 6000 系 合金28C 0.5 0.9 0.2 一 0.1 - — 0.02 — 6000 系 比 較 例 合 I 合金29C 0.9 0.1 0.5 - 0.1 - - 0.02 - 6000 系 Si未達下限値 合金30C 0.9 1.8 0.4 - 0.1 _ - 0.02 - 6000 系 Si超過上限値 合金31C 0.2 0.5 0.5 - 0.1 - — 0.02 ~ 6000 系 Mg未達下限値 合金32C 1.7 0.5 0.4 - 0.1 - 0.02 - 6000 系 Mg超過上限値 (處理） 首先，將合金2 7 C〜3 2 C依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理，製作出板厚5 00mm 的鑄塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割材 是將前述鑄塊經由切割步驟處理所得。熱壓延材，是將鑄 塊經由熱處理後進行熱壓延而製得。切割材和熱壓延材都 是厚度20mmx寬度lOOOmmx長度2000mm的銘合金厚板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材在3 5 0 °C保持4小時。 進一步，將製得的切割材及熱壓延材以5 20 °C進行熔 體化處理，然後以1 75 °C進行8小時的時效處理。 因此，前述處理後的切割材是屬於第11發明的製造 方法所製得之鋁合金厚板，前述處理後的熱壓延材則不 是。又只有使用合金27C、28C之切割材屬於第11發明的 實施例。 接著，對於前述處理後的切割材及熱壓延材，進行強 -93- 200900512 度試驗以及氧化鋁膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度2 00N/mm2以 上的情形判定爲合格（〇），將拉伸強度未達200N/mm2 的情形判定爲不合格（X )。 試驗結果顯示於表2 8。 [表 28]X i (m/lum) inch inch Ό one inch Ό i I inch Ό £s (ΝΙΓ0 (Nls (ΝΙΓ0 议 u9 (n collar as a distinction _ 莩 莩 莩 SS SS SS SS 怎 怎 怎 - - 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 91 As shown in Table 26, in the case of alloy 2 3 C~2 6 C, the processing strain is small and the bending is small, that is, the flatness is good and the plate thickness precision is excellent. In the case of alloy 25C, since the Μη content is not lower than the lower limit値, the strength is insufficient. In the case of alloy 26C, since the Μη content exceeds the upper limit 値, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloy 23 C to 26C, in the case of the alloy The appearance of the cross-section after the film treatment does not cause unevenness. (About the hot-rolled material) As shown in Table 26, in the case of the alloys 23C to 26C, the processing strain is accumulated, and the bending in the rolling direction is large, that is, the flatness is poor. The plate thickness accuracy is almost inferior to that of the cutting material. In the case of alloy 2 5 C, since the Μη content does not reach the lower limit 値, the strength is slightly worse than other hot rolled materials. In the alloy 2 6 C In the case, since the Μη content exceeds the upper limit, coarse The intermetallic compound has a non-uniform appearance on the surface after the treatment of the aluminum oxide film. In the case of the alloys 23C to 26C, the cross-sectional appearance of the aluminum oxide film after treatment is uneven. (1 4) The first embodiment This embodiment The aluminum alloy used in the present embodiment is a 6000-series Al-Mg-Si alloy. The alloys 27C and 28C shown in Table 27 were used as the alloys of the examples, and the alloys 29C to 32C were used as the alloys of the comparative examples. -92- 200900512 Table 27] Section number element (% by mass) Alloy type preparation Mg Si Fe Cu Μη Cr Ζη Ti Zr Implementation of the joint gold alloy 27C 0.9 0.5 0.5 0.3 0.1 0.2 0.2 0.02 - 6000 Alloy 28C 0.5 0.9 0.2 A 0.1 - 0.02 - 6000 series comparison example I alloy 29C 0.9 0.1 0.5 - 0.1 - - 0.02 - 6000 Si is not up to the lower limit 値 alloy 30C 0.9 1.8 0.4 - 0.1 _ - 0.02 - 6000 Si exceeds the upper limit 値 alloy 31C 0.2 0.5 0.5 - 0.1 - — 0.02 ~ 6000 Series Mg not reached the lower limit 値 alloy 32C 1.7 0.5 0.4 - 0.1 - 0.02 - 6000 Series Mg exceeds the upper limit 处理 (treatment) First, the alloy 2 7 C~3 2 C is sequentially passed through the melting step hydrogen In the steps of the steps, the filtration step and the casting step, an ingot having a thickness of 500 mm was produced. Next, a cut material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the aforementioned ingot through a cutting step. The hot rolled material is obtained by subjecting the ingot to heat rolling after heat treatment. Both the cutting material and the hot rolled material are ingot alloy thick plates having a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. That is, the above cut material was kept at 350 ° C for 4 hours. Further, the obtained cut material and hot rolled material were melted at 520 ° C, and then aged at 1 75 ° C for 8 hours. Therefore, the cut material after the above treatment is an aluminum alloy thick plate obtained by the manufacturing method of the eleventh invention, and the hot rolled material after the above treatment is not. Further, only the cutting materials using the alloys 27C and 28C belong to the embodiment of the eleventh invention. Next, the cut-off material and the hot-rolled material after the above treatment were subjected to a strong-93-200900512 degree test and an aluminum oxide film treatability evaluation test. The method and evaluation criteria of each test were the same as those in the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the strength evaluation criteria are as follows. In other words, in terms of strength, the tensile strength of 200 N/mm 2 or more was judged as pass (〇), and the tensile strength of less than 200 N/mm 2 was judged as unacceptable (X). The test results are shown in Table 28. [Table 28]

區分 編號 強度 氧化鋁膜處理後外觀 拉伸強度 (N/mm2) 安全限應力 (N/mm2) 判定 表面外觀 截面外觀 實 合金27C 317 269 〇 〇 〇 施 合金28C 290 247 〇 〇 〇 切 例 割 比 合金29C 110 64 X 〇 〇 材 合金30C 335 298 〇 X 〇 較 tCt\ 合金31C 172 120 X 〇 〇 例 合金32C 209 123 〇 〇 〇 合金27C 343 272 〇 〇 X 熱 比 合金28C 316 272 〇 〇 X 壓 合金29C 132 84 X 〇 X 延 較 合金30C 359 319 〇 X X 材 例 合金31C 197 142 X 〇 X 合金32C 228 141 〇 〇 X (關於切割材） 如表2 8所示，在合金2 9 C、3 1 C的情形，由於S i、 -94- 200900512Distinguishing the tensile strength of the numbered strength alumina film after treatment (N/mm2) Safety limit stress (N/mm2) Judging the appearance of the surface appearance of the solid alloy 27C 317 269 〇〇〇 Application alloy 28C 290 247 Cutting ratio cutting ratio Alloy 29C 110 64 X Coffin Alloy 30C 335 298 〇X 〇Compared tCt\ Alloy 31C 172 120 X 〇〇Example Alloy 32C 209 123 〇〇〇Alloy 27C 343 272 〇〇X Thermal Ratio Alloy 28C 316 272 〇〇X Pressure Alloy 29C 132 84 X 〇X Extension alloy 30C 359 319 〇XX Material alloy 31C 197 142 X 〇X Alloy 32C 228 141 〇〇X (About cutting material) As shown in Table 2, in alloy 2 9 C, 3 1 C case, due to S i, -94- 200900512

Mg含量分別未達下限値’強度不足。在合金30C的情 形，由於S i含量超過上限値，會生成粗大的金屬間化合 物，氧化鋁膜處理後的表面外觀發生不均勻。在合金32C 的情形，由於Mg含量超過上限値，Mg效果達飽和，經濟 性差。在合金27C〜3 2C的情形，在氧化鋁膜處理後的截 面外觀不會發生不均勻。 (關於熱壓延材） 如表2 8所示，在合金2 9 C、3 1C的情形，由於S i、 Mg含量分別未達下限値，強度不足。在合金30C的情 形，由於Si含量超過上限値，會生成粗大的金屬間化合 物，氧化鋁膜處理後的表面外觀發生不均勻。在合金32C 的情形，由於M g含量超過上限値，M g效果達飽和，經濟 性差。在合金27C〜3 2C的情形，在氧化鋁膜處理後的截 面外觀會發生不均勻。 (1 5 )第1 5實施例 本實施例是關於第12發明。本實施例使用的鋁合 金，是7000系的Al-Zn-Mg系合金。 使用表29所示的合金33C、34C作爲實施例合金，使 用合金35C〜38C作爲比較例合金。 -95- 200900512 ^ ^ J 元素(質量％) 合余 備考 區分 編號 Mg Si Fe Cu Μη Cr Zn Ti Zr _ 實 合金33C 9 4 0.1 0.2 1.8 — 0.2 4.0 0.02 - 7000 系 施合 例余 合金34C 3.6 0.2 0.2 2.0 — - 8.0 0.02 0.2 7000 系 LL 合金35C 0.3 0.1 0.2 2.2 — 0.1 4.0 0.02 - 7000 系 Mg未達下限値 ft 合金36C 5 2 0.2 0.2 2.0 0.1 5.0 0.02 - 7000 系 Mg超過上限値 例 合金37C 7.4 0.1 0.2 2.2 0.1 2.4 0.02 - 7000系彳 Zn未達下限値 金 合金38C 3.0 0.2 0.2 2.0 0.1 9.5 0.02 - 7000 系 Zn超過上限値 (處理） 首先，將合金33C〜38C依序經由熔解步驟、脫氫氣 步驟、過濾步驟及鑄造步驟的處理’製作出板厚500mm 的鑄塊。 接著，從前述鑄塊製作出切割材和熱壓延材。切割材· 是將前述鑄塊經由切割步驟處理所得。熱壓延材，是將前 述鑄塊經由熱處理後進行熱壓延而製得。切割材和熱壓延 材都是厚度20mmx寬度lOOOmmx長度2000mm的銘合金厚 板。 接著，將前述切割材藉由熱處理步驟進行處理。亦 即，將前述切割材在3 0 0 °C保持4小時。 進一步，將製得的切割材及熱壓延材以470 °C進行熔 體化處理，然後以1 2 0。(：進行4 8小時的時效處理。 因此，前述處理後的切割材是屬於第1 2發明的製造 方法所製得之鋁合金厚板，前述處理後的熱壓延材則不 是。又只有使用合金33C、34C之切割材屬於第12發明的 實施例。 -96- 200900512 接著，對於前述處理後的切割材及熱壓延材，進行強 度試驗以及氧化鋁膜處理性評價試驗。 各試驗的方法及評價基準是和第1實施例的情形相 同。 由於厚板特性會依合金種類而有不同，故強度的評價 基準如下。亦即，在強度方面，將拉伸強度2 5 0N/mm2以 上的情形判定爲合格（〇），將拉伸強度未達25 0N/mm2 的情形判定爲不合格（X )。 試驗結果顯示於表3 0。 [表 30]The Mg content is less than the lower limit, respectively, and the strength is insufficient. In the case of the alloy 30C, since the Si content exceeds the upper limit 粗, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloy 32C, since the Mg content exceeds the upper limit M, the Mg effect is saturated and the economy is poor. In the case of the alloys 27C to 3 2C, the cross-sectional appearance after the treatment of the aluminum oxide film did not occur unevenly. (About hot rolled material) As shown in Table 2, in the case of the alloys 2 9 C and 3 1C, since the Si and Mg contents are not at the lower limit, the strength is insufficient. In the case of the alloy 30C, since the Si content exceeds the upper limit 粗, a coarse intermetallic compound is formed, and the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of Alloy 32C, since the Mg content exceeds the upper limit 値, the Mg effect is saturated and the economy is poor. In the case of the alloys 27C to 3 2C, the cross-sectional appearance after the treatment of the aluminum oxide film may be uneven. (1 5) The fifteenth embodiment This embodiment relates to the twelfth invention. The aluminum alloy used in the present embodiment is a 7000-series Al-Zn-Mg-based alloy. Alloys 33C and 34C shown in Table 29 were used as the alloys of the examples, and alloys 35C to 38C were used as the alloys of the comparative examples. -95- 200900512 ^ ^ J Element (% by mass) Balanced Pro Forma Division No. Mg Si Fe Cu Μη Cr Zn Ti Zr _ Real Alloy 33C 9 4 0.1 0.2 1.8 — 0.2 4.0 0.02 - 7000 System Application Example Alloy 34C 3.6 0.2 0.2 2.0 — — 8.0 0.02 0.2 7000 Series LL Alloy 35C 0.3 0.1 0.2 2.2 — 0.1 4.0 0.02 - 7000 Series Mg has not reached the lower limit 値 ft alloy 36C 5 2 0.2 0.2 2.0 0.1 5.0 0.02 - 7000 Series Mg exceeds the upper limit Example Alloy 37C 7.4 0.1 0.2 2.2 0.1 2.4 0.02 - 7000 彳 彳 未 未 値 値 38 38 38 38C 3.0 0.2 0.2 2.0 0.1 9.5 0.02 - 7000 Zn exceeds the upper limit 处理 (treatment) First, the alloy 33C~38C sequentially through the melting step, dehydrogenation Step, filtration step, and treatment of the casting step 'Ingots having a thickness of 500 mm were produced. Next, a cut material and a hot rolled material were produced from the above ingot. The cutting material is obtained by treating the ingot described above through a cutting step. The hot rolled material is obtained by subjecting the ingot to heat rolling after heat treatment. Both the cutting material and the hot rolled material are thick alloy plates with a thickness of 20 mm x a width of 1000 mm and a length of 2000 mm. Next, the aforementioned cutting material is treated by a heat treatment step. That is, the above cut material was kept at 300 ° C for 4 hours. Further, the obtained cut material and hot rolled material were melted at 470 ° C, and then 1 2 0. (: The aging treatment is carried out for 48 hours. Therefore, the cut material after the treatment is an aluminum alloy thick plate obtained by the production method of the first invention, and the hot rolled material after the treatment is not. The cutting materials of the alloys 33C and 34C belong to the embodiment of the twelfth invention. -96- 200900512 Next, the strength test and the aluminum oxide film treatability evaluation test were performed on the cut material and the hot rolled material after the above treatment. The evaluation criteria are the same as in the case of the first embodiment. Since the characteristics of the thick plate vary depending on the type of the alloy, the evaluation criteria of the strength are as follows. That is, the tensile strength is 2500 N/mm 2 or more in terms of strength. The case was judged as pass (〇), and the case where the tensile strength was less than 25 0 N/mm 2 was judged as unacceptable (X). The test results are shown in Table 30. [Table 30]

區分 編號 強度 氧化鋁膜處理後外觀 拉伸強度 (N/mm2) 安全限應力 (N/mm2) 判定 表面外觀 截面外觀 切 割 材 實 施 例 合金33C 418 360 〇 〇 〇 合金34C 520 453 〇 〇 〇 比 較 例 合金35C 189 162 X 〇 〇 合金36C 290 190 〇 X 〇 合金37C 208 131 X 〇 〇 合金38C 614 530 〇 X 〇 熱 壓 延 材 比 較 例 合金33C 437 378 〇 〇 X 合金34C 549 478 〇 〇 X 合金35C 204 169 X 〇 X 合金36C 305 204 〇 X X 合金37C 230 150 X 〇 X 合金38C 628 542 〇 X X (關於切割材） 如表30所示，在合金35C、37C的情形，由於Mg、 -97- 200900512Distinguishing the strength of the aluminum alloy film after treatment. Tensile strength (N/mm2) Safety limit stress (N/mm2) Judging surface appearance Cross-section appearance Cutting material Example alloy 33C 418 360 Niobium alloy 34C 520 453 〇〇〇Comparative example Alloy 35C 189 162 X 〇〇 alloy 36C 290 190 〇X 〇 alloy 37C 208 131 X 〇〇 alloy 38C 614 530 〇X 〇 hot rolled material comparative example alloy 33C 437 378 〇〇X alloy 34C 549 478 〇〇X alloy 35C 204 169 X 〇X Alloy 36C 305 204 〇XX Alloy 37C 230 150 X 〇X Alloy 38C 628 542 〇XX (About cutting material) As shown in Table 30, in the case of Alloys 35C and 37C, due to Mg, -97- 200900512

Zn含量分別未達下限値，強度不足。在合金36C、38C的 情形，由於Mg、Zn含量分別超過上限値，氧化鋁膜處理 後的表面外觀發生不均句。在合金33C〜38C的情形，在 氧化鋁膜處理後的截面外觀不會發生不均勻。 (關於熱壓延材） 如表3 0所示’在合金3 5 C、3 7 C的情形，由於M g、The Zn content is less than the lower limit and the strength is insufficient. In the case of alloys 36C and 38C, since the contents of Mg and Zn exceed the upper limit, respectively, the surface appearance after the treatment of the alumina film is uneven. In the case of the alloys 33C to 38C, the cross-sectional appearance after the treatment of the aluminum oxide film did not occur unevenly. (About hot rolled material) as shown in Table 30. In the case of alloys 3 5 C, 3 7 C, due to Mg,

Zn含量分別未達下限値，強度不足。在合金36C、38C的 情形，由於Mg、Zn含量分別超過上限値，氧化鋁膜處理 後的表面外觀發生不均勻。在合金33C〜38C的情形，在 氧化鋁膜處理後的截面外觀會發生不均勻。 本申請發明的鋁合金厚板之製造方法，具有優異的生 產性，容易控制表面狀態及平坦度，可提昇板厚精度，因 此產業上的利用價値高。 【圖式簡單說明】 第1圖係顯示第1至第4發明及第9至第12發明之 銘合金厚板之製造方法之流程圖。 第2圖係顯示在切割步驟除去的鑄塊的厚度方向中央 部分之示意圖。 第3圖係顯示第5至第8發明之鋁合金厚板之製造方 法之流程圖。 【主要元件符號說明】 -98- 200900512 s 1 :熔解步驟 S 2 :脫氫氣步驟 S 3 :過瀘步驟 S4 :鑄造步驟 S 5 :切割步驟或熱處理步驟 S 6 :熱處理步驟或切割步驟 S7 :表面平滑化處理步驟 A :厚度方向中央 B:厚度方向中央部分 T :厚度 1 : f帚塊 -99-The Zn content is less than the lower limit and the strength is insufficient. In the case of the alloys 36C and 38C, since the Mg and Zn contents respectively exceed the upper limit 値, the surface appearance after the treatment of the aluminum oxide film is uneven. In the case of the alloys 33C to 38C, the cross-sectional appearance after the treatment of the aluminum oxide film may be uneven. The method for producing an aluminum alloy thick plate according to the present invention has excellent productivity, can easily control the surface state and flatness, and can improve the thickness accuracy, so that the industrial use price is high. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a flow chart showing a method of manufacturing the alloy plate of the first to fourth inventions and the ninth to twelfth inventions. Fig. 2 is a view showing a central portion in the thickness direction of the ingot removed at the cutting step. Fig. 3 is a flow chart showing a method of manufacturing the aluminum alloy thick plate of the fifth to eighth inventions. [Description of main component symbols] -98- 200900512 s 1 : Melting step S 2 : Dehydrogenation step S 3 : Overpassing step S4 : Casting step S 5 : Cutting step or heat treatment step S 6 : Heat treatment step or cutting step S7: Surface Smoothing process step A: center in the thickness direction B: center portion in the thickness direction T: thickness 1: f帚 block-99-

Claims (1)

200900512 十、申請專利範圍 1_ 一種鋁合金厚板之製ia方法，係從錦合金製造出銘 合金厚板的方法，其特徵在於： 前述鋁合金，係含有M g : 1 · 5質量％〜1 2.0質量％， 且含有選自Si : 0.7質量％以下、Fe : 0.8質量％以下、 Cu : 0.6質量％以下、Μη : 1.0質量％以下、Cr : 0·5質量 %以下、Ζη : 0.4質量％以下、Ti : 〇.1質量％以下、Zr : 0.3質量％以下中之至少1種’剩餘部分爲A1及不可避免 的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 割步驟、 將既定厚度的鋁合金厚板以400 以上未達瑢點的溫 度保持1小時以上來進行熱處理之熱處理步驟。 2. —種鋁合金厚板之製造方法’係從鋁合金製造出鋁 合金厚板的方法，其特徵在於： 前述鋁合金’係含有Mn : 0 ·3質量％〜1 ·6質鼍％，且 含有選自Si : 0.7質量％以下、Fe : 0.8質量％以下、Cu : 0 · 5質量％以下、M g : 1 . 5質量％以下、C r : 0 · 3質量％以 下、Ζ η : 0.4質量％以下、T i : 0 ·1質量％以下、z r : 〇 . 3質 -100- 200900512 量％以下中之至少1種，剩餘部分爲A1及不可避免的雜質 所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 割步驟、 將既定厚度的鋁合金厚板以40(TC以上未達熔點的溫 度保持1小時以上來進行熱處理之熱處理步驟。 3.—種鋁合金厚板之製造方法，係從鋁合金製造出鋁 合金厚板的方法，其特徵在於： 前述鋁合金，係含有S i : 0 · 2質量％〜1 . 6質量％、 Mg : 0.3質量％〜1.5質量％，且含有選自Fe : 0.8質量％ 以下、C u : 1 · 0質量％以下、Μ η : 0 · 6質量％以下、C r : 0.5質量％以下、Zn : 0.4質量％以下、Ti : 0. 1質量％以 下、Zr : 0.3質量％以下中之至少1種，剩餘部分爲A1及 不可避免的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 -101 - 200900512 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 割步驟、 將既定厚度的鋁合金厚板以4 0 0 °c以上未達熔點的溫 度保持1小時以上來進行熱處理之熱處理步驟。 4 . 一種鋁合金厚板之製造方法’係從鋁合金製造出鋁 合金厚板的方法，其特徵在於： 前述鋁合金，係含有Mg: 〇.4質量％〜4·0質量％、 Zn : 3.0質量％〜9.0質量％ ’且含有選自Si : 0.7質量％以 下' Fe: 0.8質量％以下、Cu: 3.0質量％以下、Μη: 0.8 質量％以下、C r : 0.5質量％以下、T i : 0 · 1質量％以下、 Z r : 0.2 5質量％以下中之至少1種，剩餘部分爲A 1及不可 避免的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 割步驟、 將既定厚度的鋁合金厚板以3 5 0 °C以上未達熔點的溫 度保持1小時以上來進行熱處理之熱處理步驟。 5 ·如申請專利範圍第1至4項中任一項記載之鋁合金 厚板之製造方法，其中，在前述熱處理步驟後，進行表面 平滑化處理步驟，以對鋁合金厚板的表面實施表面平滑化 -102- 200900512 處理。 6.如申請專利範圍第5項記載之銘合金厚板之製造方 法，其中’前述表面平滑化處理，是以選自切削法、磨削 法及硏磨法中之1種以上的方法來進行。 7 _如申請專利範圍第1至4項中任一項記載之鋁合金 厚板之製造方法’其中，在前述切割步驟中，將厚度方向 中央部分從前述鑄塊除去；該厚度方向中央部分，是從厚 度方向中央朝厚度方向之各表面具有均等的厚度，且設前 述鑄塊厚度爲T的情形，合計具有T/30〜T/5的厚度。 8 · —種鋁合金厚板之製造方法，係從鋁合金製造出鋁 合金厚板的方法，其特徵在於： 前述鋁合金，係含有Mg : 1 . 5質量％〜1 2 · 0質量％， 且含有選自 Si : 0.7質量％以下、Fe : 0.8質量％以下、 Cu ·· 0.6質量％以下、Mn : 1 0質量％以下、Cr ·· 0.5質量 %以下、Zn : 0.4質量％以下、Ti : 0.1質量％以下、Zr : 0 · 3質量％以下中之至少1種，剩餘部分爲A1及不可避免 的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟' 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟' 將前述鑄塊以20(TC以上未達40〇r的溫度保持1小 時以上來進行熱處理之熱處理步驟、 -103- 200900512 將熱處理後的鑄塊切割而製造成既定厚度的鋁合金厚 板之切割步驟。 9. 一種鋁合金厚板之製造方法，係從鋁合金製造出鋁 合金厚板的方法，其特徵在於： 前述銘合金，係含有Μη: 0.3質量％〜1.6質量％，且 含有選自Si : 0.7質量％以下' Fe : 0.8質量％以下、Cu : 0 · 5質量％以下、M g : 1 · 5質量％以下、C r : 0 · 3質量％以 下、Zn : 0.4質量％以下、Ti : 0.1質量％以下、Zr : 0.3質 量％以下中之至少1種，剩餘部分爲A1及不可避免的雜質 所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊以2 0 0 °C以上未達4 0 0 °C的溫度保持1小 時以上來進行熱處理之熱處理步驟、 將熱處理後的鑄塊切割而製造成既定厚度的鋁合金厚 板之切割步驟。 10. —種鋁合金厚板之製造方法，係從鋁合金製造出 鋁合金厚板的方法，其特徵在於： 前述鋁合金，係含有s i : 0 · 2質量％〜1 · 0質量％、 Mg: 0.3質量％〜1.5質量％ ’且含有選自Fe: 〇_8質量％ 以下、C u : 1 . 0質量％以下、M n : 〇 · 6質量％以下、C Γ ·· -104- 200900512 〇 . 5質量％以下、Ζ η : 0.4質量％以下、T i : 〇 . 1質量％以 下、Z r : 0 · 3質量％以下中之至少1種，剩餘部分爲A1及 不可避免的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟' 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟' 將前述鑄塊以2 0 0 °C以上未達4 0 0 °C的溫度保持1小 時以上來進行熱處理之熱處理步驟、 將熱處理後的鑄塊切割而製造成既定厚度的鋁合金厚 板之切割步驟。 11. 一種銘合金厚板之製造方法，係從銘合金製造出 鋁合金厚板的方法，其特徵在於： 前述鋁合金，係含有Mg: 0.4質量％〜4.0質量％、 Zn: 3.0質量°/。〜9.0質量％，且含有選自Si: 0.7質量％以 下、Fe: 0.8質量％以下、Cu: 3.0質量％以下、Μη: 0.8 質量％以下、Cr : 0.5質量％以下、Ti : 0· 1質量％以下、 Zr : 0.25質量％以下中之至少1種，剩餘部分爲A1及不可 避免的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 -105- 200900512 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊以2 00t以上未達35(TC的溫度保持1小 時以上來進行熱處理之熱處理步驟、 將熱處理後的鑄塊切割而製造成既定厚度的鋁合金厚 板之切割步驟。 1 2.如申請專利範圍第8至i 1項中任一項記載之鋁合 金厚板之製造方法，其中，在前述切割步驟後，進行表面 平滑化處理步驟，以對既定厚度的鋁合金厚板的表面實施 表面平滑化處理。 1 3 .如申請專利範圍第1 2項記載之鋁合金厚板之製造 方法，其中，前述表面平滑化處理，是以選自切削法、磨 削法及硏磨法中之1種以上的方法來進行。 1 4.如申請專利範圍第8至1 1項中任一項記載之鋁合 金厚板之製造方法，其中，在前述切割步驟中，將厚度方 向中央部分從前述鑄塊除去；該厚度方向中央部分，是從 厚度方向中央朝厚度方向之各表面具有均等的厚度，且設 前述鑄塊厚度爲T的情形’合計具有T/3 0〜T/5的厚度。 1 5 . —種鋁合金厚板之製造方法，係從鋁合金製造出 鋁合金厚板的方法’其特徵在於： 前述鋁合金’係含有Mg : 1.5質量％〜12.0質量％ ’ 且含有選自Si: 0.7質量％以下、Fe: 0_8質量。/。以下、 Cu: 0.6質量％以下、Mn:丨·0質量°/。以下、Cr: 〇.5質量 %以下、Zn : 0.4質量％以下、Ti : 0.1質量％以下、Zr : 0.3質量％以下中之至少1種’剩餘部分爲A1及不可避免 -106- 200900512 的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 割步驟、 將既定厚度的鋁合金厚板以200 °C以上未達400 °C的 溫度保持1小時以上來進行熱處理之熱處理步驟。 1 6 . —種鋁合金厚板之製造方法，係從鋁合金製造出 鋁合金厚板的方法，其特徵在於： 前述鋁合金，係含有Μη : 0.3質量％〜1 .6質量％，且 含有選自Si : 0.7質量％以下、Fe : 0.8質量％以下、Cu : 0.5質量％以下、M g : 1 . 5質量％以下、C r : 0.3質量％以 下、Zn : 0.4質量％以下、Ti : 0.1質量％以下、Zr : 0.3質 量％以下中之至少1種，剩餘部分爲A1及不可避免的雜質 所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的溶解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過濾步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 -107- 200900512 割步驟、 將既定厚度的鋁合金厚板以200°C以上未達400°C的 溫度保持1小時以上來進行熱處理之熱處理步驟。 1 7 · —種鋁合金厚板之製造方法，係從鋁合金製造出 鋁合金厚板的方法，其特徵在於： 前述鋁合金，係含有S i : 0.2質量％〜1 .6質量％、 Mg: 0.3質量％〜1.5質量％，且含有選自 Fe: 0.8質量％ 以下、Cu : 1 ·0質量％以下、Μη : 0.6質量％以下、Cr : 0.5質量％以下、Zn : 0.4質量％以下、Ti : 0.1質量％以 下、Zr : 0.3質量％以下中之至少1種，剩餘部分爲A1及 不可避免的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的鋁合金除去氫氣之脫氫氣步驟、 從除去氫氣後的鋁合金除去夾雜物之過瀘步驟、 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄造步驟、 將前述鑄塊切割而製造成既定厚度的鋁合金厚板之切 割步驟、 將既定厚度的鋁合金厚板以200°C以上未達400°C的 溫度保持1小時以上來進行熱處理之熱處理步驟。 1 8 . —種鋁合金厚板之製造方法，係從鋁合金製造出 鋁合金厚板的方法，其特徵在於= 前述銘合金，係含有Mg: 0.4質量％〜4.0質量％、 Zn: 3.0質量％〜9.0質量％，且含有選自Si: 0.7質量％以 -108- 200900512 下、Fe: 0.8質量。/«·以下、Cu· 3.0質量％#〒 質量％以下、C r : 〇 . 5質量％以下、T i : 0 · 1質 Z r : 0 · 2 5質量％以下中之至少1種’剩餘部分怎 避免的雜質所構成； 並且是依序進行以下步驟： 將前述鋁合金熔解的熔解步驟、 從熔解後的銘合金除去氫氣之脫氫氣步驟 從除去氫氣後的銘合金除去夾雜物之過濾^ 將除去夾雜物後的鋁合金鑄造成鑄塊之鑄^ 將前述鑄塊切割而製造成既定厚度的鋁合 割步驟、 將既定厚度的鋁合金厚板以200°C以上未 溫度保持1小時以上來進行熱處理之熱處理步局 19. 如申請專利範圍第15至18項中任一 合金厚板之製造方法，其中，在前述熱處理步 表面平滑化處理步驟，以對鋁合金厚板的表面 滑化處理。 20. 如申請專利範圍第1 9項記載之鋁合金 方法，其中’前述表面平滑化處理，是以選自 削法及硏磨法中之1種以上的方法來進行。 21. 如申請專利範圍第15至18項中任一 合金厚板之製造方法，其中，在前述切割步驟 方向中央部分從前述鑄塊除去；該厚度方向中 從厚度方向中央朝厚度方向之各表面具有均等 、Μη : 0.8 量％以下、 Α1及不可 梦驟、 g步驟、 金厚板之切 達 3 50 °C的 聚。 項記載之鋁 驟後，進行 實施表面平 厚板之製造 切削法、磨 項記載之鋁 中，將厚度 央部分，是 的厚度，且 -109- 200900512 設前述鑄塊厚度爲τ的情形，合計具有T/30〜T/5的厚 度。 22 . —種鋁合金厚板，其特徵在於：係藉由申請專利 範圍第1至4項、第8至1 1項及第1 5至1 8項中任一項 記載之鋁合金厚板之製造方法所製造出之鋁合金厚板，且 具有4 0 0 // m以下的平均結晶粒徑。 -110-200900512 X. Patent application scope 1_ A method for manufacturing aluminum alloy thick plate, which is a method for manufacturing a thick alloy plate from a nylon alloy, characterized in that: the foregoing aluminum alloy contains M g : 1 · 5 mass % ~ 1 2.0% by mass, and is selected from Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.6% by mass or less, Μη: 1.0% by mass or less, Cr: 5% by mass or less, and Ζη: 0.4% by mass. In the following, at least one of Ti: 〇1% by mass or less and Zr: 0.3% by mass or less, the remaining portion is composed of A1 and unavoidable impurities; and the following steps are sequentially performed: melting of the aluminum alloy by melting a step of removing hydrogen from the molten aluminum alloy, a step of removing impurities from the aluminum alloy after removing the hydrogen, a casting step of casting the aluminum alloy after removing the inclusions into an ingot, and cutting the ingot And a heat-treating step of heat-treating the aluminum alloy thick plate having a predetermined thickness and heat-treating the aluminum alloy thick plate having a predetermined thickness at a temperature of 400 or more and less than 1 hour. . 2. A method for producing an aluminum alloy thick plate as a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy ' contains Mn: 0 · 3 mass % to 1 · 6 mass %, Further, it is selected from the group consisting of Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.5% by mass or less, Mg: 1.5% by mass or less, Cr: 0·3 mass% or less, and Ζ η: 0.4 mass% or less, T i : 0 · 1 mass % or less, zr : 〇. 3 mass -100 - 200900512 at least one of the following: %, and the remainder is composed of A1 and unavoidable impurities; The following steps are carried out: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, a filtration step of removing inclusions from the aluminum alloy after removing hydrogen, and casting the aluminum alloy from which the inclusions are removed a casting step of the ingot, a cutting step of cutting the ingot to produce an aluminum alloy thick plate having a predetermined thickness, and heat-treating the aluminum alloy thick plate having a predetermined thickness by 40 (TC or more at a temperature not exceeding the melting point for 1 hour or more) Heat treatment step 3. A method for producing an aluminum alloy thick plate, which is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that: the aluminum alloy contains S i : 0 · 2 mass % to 1. 6 mass % Mg: 0.3% by mass to 1.5% by mass, and is selected from the group consisting of Fe: 0.8% by mass or less, C u : 1 · 0 mass% or less, Μ η: 0 · 6 mass% or less, and C r : 0.5 mass% or less. At least one of Zn: 0.4% by mass or less, Ti: 0.1% by mass or less, and Zr: 0.3% by mass or less, and the remainder is composed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, a filtration step of removing the inclusions from the aluminum alloy after removing the hydrogen, a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, -101 - 200900512 The cutting step of cutting the ingot to produce an aluminum alloy thick plate of a predetermined thickness, and heat-treating the aluminum alloy thick plate of a predetermined thickness at a temperature of not more than 40 ° C for 1 hour or more for heat treatment Heat Step 4. A method for producing an aluminum alloy thick plate is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy contains Mg: 〇. 4% by mass to 4.0% by mass Zn: 3.0% by mass to 9.0% by mass ', and is selected from Si: 0.7% by mass or less 'Fe: 0.8% by mass or less, Cu: 3.0% by mass or less, Μη: 0.8% by mass or less, and Cr: 0.5% by mass or less At least one of T i : 0 · 1 mass % or less, Z r : 0.2 5 mass % or less, and the remainder is composed of A 1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, a filtration step of removing inclusions from the aluminum alloy after removing hydrogen, and a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, A step of cutting the aluminum alloy thick plate having a predetermined thickness by cutting the ingot, and a heat treatment step of heat-treating the aluminum alloy thick plate having a predetermined thickness at a temperature of not more than 350 ° C for 1 hour or more. The method for producing an aluminum alloy thick plate according to any one of claims 1 to 4, wherein after the heat treatment step, a surface smoothing treatment step is performed to apply a surface to the surface of the aluminum alloy thick plate. Smoothing -102- 200900512 Processing. 6. The method for producing a thick alloy plate according to the fifth aspect of the invention, wherein the surface smoothing treatment is performed by one or more selected from the group consisting of a cutting method, a grinding method, and a honing method. . The method for producing an aluminum alloy thick plate according to any one of claims 1 to 4, wherein in the cutting step, the central portion in the thickness direction is removed from the ingot; the central portion in the thickness direction, The thickness of each of the surfaces in the thickness direction from the center in the thickness direction has a uniform thickness, and the thickness of the ingot is T, and the total thickness is T/30 to T/5. And a method for producing an aluminum alloy thick plate, wherein the aluminum alloy contains Mg: 1.5% by mass to 1 2 · 0 mass%, Further, it is selected from Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu··0.6% by mass or less, Mn: 100% by mass or less, Cr··0.5% by mass or less, and Zn: 0.4% by mass or less, Ti. : 0.1% by mass or less, at least one of Zr: 0 · 3 mass % or less, and the remainder is composed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting the aluminum alloy described above, The dehydrogenation step of removing the hydrogen gas from the molten aluminum alloy, the filtration step of removing the inclusions from the aluminum alloy after removing the hydrogen gas, the casting step of casting the aluminum alloy from the inclusions into the ingot, and the ingot is 20 (TC) The heat treatment step of heat treatment for which the temperature of less than 40 〇r is maintained for 1 hour or more, -103-200900512 The step of cutting the heat-treated ingot to produce a thick aluminum alloy plate having a predetermined thickness. The method for producing a thick plate is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the alloy is Μη: 0.3% by mass to 1.6% by mass and contains Si: 0.7% by mass or less. Fe: 0.8% by mass or less, Cu: 0·5 mass% or less, M g : 1 · 5 mass% or less, C r : 0 · 3 mass% or less, Zn: 0.4 mass% or less, and Ti: 0.1 mass% or less, Zr: at least one of 0.3% by mass or less, the remainder being composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: a melting step of melting the aluminum alloy, and removing hydrogen from the molten aluminum alloy a dehydrogenation step, a filtration step of removing inclusions from the aluminum alloy after removing the hydrogen gas, a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, and the ingot is not more than 200°C. A heat treatment step of heat treatment at a temperature of ° C for 1 hour or more, and a step of cutting the heat-treated ingot to produce a thick aluminum alloy plate having a predetermined thickness. 10. A method for producing an aluminum alloy thick plate A method for producing an aluminum alloy thick plate of an aluminum alloy, characterized in that the aluminum alloy contains si: 0 · 2 mass % to 1 · 0 mass %, Mg: 0.3 mass % - 1.5 mass % ' and contains a selected from Fe : 〇 _ 8 mass % or less, C u : 1.0 mass % or less, M n : 〇 · 6 mass % or less, C Γ ·· -104- 200900512 〇. 5 mass% or less, Ζ η : 0.4 mass% or less And T i : 〇. 1% by mass or less, Z r : 0 · 3 mass % or less, at least one of the remaining portions, and the remainder is composed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting, a dehydrogenation step of removing hydrogen from the molten aluminum alloy, and a filtration step of removing inclusions from the aluminum alloy after removing hydrogen; a casting step of casting an aluminum alloy after removing the inclusion into an ingot. The ingot is subjected to a heat treatment step of heat treatment at a temperature of 200 ° C or higher and less than 400 ° C for 1 hour or more, and a step of cutting the heat-treated ingot to produce a thick aluminum alloy plate having a predetermined thickness. 11. A method for producing a thick alloy plate, which is a method for producing an aluminum alloy thick plate from an alloy, characterized in that: the aluminum alloy contains Mg: 0.4% by mass to 4.0% by mass, and Zn: 3.0% by mass/ . ～9.0% by mass, and is selected from the group consisting of Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 3.0% by mass or less, Μη: 0.8% by mass or less, Cr: 0.5% by mass or less, and Ti: 0·1 mass. % or less, Zr: at least one of 0.25 mass% or less, the remainder being composed of A1 and unavoidable impurities; and the following steps are sequentially performed: a melting step of melting the aluminum alloy, and a molten aluminum alloy a hydrogen removal step for removing hydrogen gas, a filtration step for removing inclusions from an aluminum alloy after removing hydrogen gas, -105-200900512, a casting step of casting an aluminum alloy into an ingot after removing inclusions, and the ingot is not more than 200 tons a step of cutting up to 35 (the heat treatment step in which the temperature of the TC is maintained for 1 hour or more, and the ingot after the heat treatment is cut to produce a thick aluminum alloy plate having a predetermined thickness. 1 2. For the patent application range 8 to i 1 The method for producing an aluminum alloy thick plate according to any one of the preceding claims, wherein, after the cutting step, a surface smoothing treatment step is performed to form a surface of the aluminum alloy thick plate having a predetermined thickness The method for producing an aluminum alloy thick plate according to claim 12, wherein the surface smoothing treatment is selected from the group consisting of a cutting method, a grinding method, and a honing method. The method for producing an aluminum alloy thick plate according to any one of claims 8 to 11, wherein in the cutting step, the central portion in the thickness direction is The ingot is removed; the central portion in the thickness direction has a uniform thickness from the center in the thickness direction toward each surface in the thickness direction, and the thickness of the ingot is T is 'the total thickness of T/3 0 to T/5. A method for producing an aluminum alloy thick plate, which is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that: the aluminum alloy ' contains Mg: 1.5% by mass to 12.0% by mass' and contains From Si: 0.7% by mass or less, Fe: 0_8 mass% or less, Cu: 0.6% by mass or less, Mn: 丨·0 mass%/. or less, Cr: 〇.5 mass% or less, and Zn: 0.4 mass% or less , Ti : 0.1% by mass or less, Zr: 0.3% by mass At least one of the following is composed of impurities of A1 and unavoidable -106-200900512; and the following steps are sequentially performed: a melting step of melting the aluminum alloy, and removing hydrogen from the molten aluminum alloy a hydrogen step, a filtration step of removing inclusions from an aluminum alloy after removing hydrogen, a casting step of casting an aluminum alloy from which inclusions are removed into an ingot, and cutting the ingot to produce a cut of an aluminum alloy thick plate having a predetermined thickness In the step, a heat treatment step of heat treatment is performed by holding a thick aluminum alloy plate of a predetermined thickness at a temperature of 200 ° C or more and less than 400 ° C for 1 hour or more. A method for producing an aluminum alloy thick plate, which is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy contains Μη: 0.3% by mass to 1.6% by mass, and contains It is selected from Si: 0.7% by mass or less, Fe: 0.8% by mass or less, Cu: 0.5% by mass or less, Mg: 1.5% by mass or less, Cr: 0.3% by mass or less, and Zn: 0.4% by mass or less, Ti: At least one of 0.1% by mass or less and Zr: 0.3% by mass or less, and the remainder is composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: a dissolution step of melting the aluminum alloy, and after melting a dehydrogenation step of removing aluminum gas from an aluminum alloy, a filtration step of removing inclusions from an aluminum alloy after removing hydrogen, a casting step of casting an aluminum alloy from which inclusions are removed into an ingot, and cutting the ingot to have a predetermined thickness Cutting of aluminum alloy thick plate -107- 200900512 The heat-treating step of heat treatment is carried out by cutting the aluminum alloy thick plate of a predetermined thickness at a temperature of 200 ° C or more and less than 400 ° C for 1 hour or more. The method for producing an aluminum alloy thick plate is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that the aluminum alloy contains S i : 0.2% by mass to 1.6% by mass, Mg 0.3% by mass to 1.5% by mass, and is selected from the group consisting of Fe: 0.8% by mass or less, Cu: 1·0% by mass or less, Μη: 0.6% by mass or less, Cr: 0.5% by mass or less, and Zn: 0.4% by mass or less. At least one of Ti: 0.1% by mass or less and Zr: 0.3% by mass or less, and the remainder is composed of A1 and unavoidable impurities; and the following steps are carried out in sequence: a melting step of melting the aluminum alloy, and melting a step of dehydrogenating hydrogen gas from the rear aluminum alloy, a step of removing inclusions from the aluminum alloy after removing the hydrogen gas, a casting step of casting the aluminum alloy from which the inclusions are removed into an ingot, and cutting the ingot to produce The step of cutting the aluminum alloy thick plate of a predetermined thickness, and the heat treatment step of heat-treating the aluminum alloy thick plate of a predetermined thickness at a temperature of 200 ° C or more and less than 400 ° C for 1 hour or more. 1 8 . A method for producing an aluminum alloy thick plate, which is a method for producing an aluminum alloy thick plate from an aluminum alloy, characterized in that: the above-mentioned alloy, containing Mg: 0.4% by mass to 4.0% by mass, Zn: 3.0 mass % to 9.0% by mass, and contains a material selected from the group consisting of Si: 0.7% by mass and -108-200900512, and Fe: 0.8 mass. /«·Following, Cu·3.0 mass%#〒 mass% or less, C r : 〇. 5 mass% or less, T i : 0 · 1 mass Z r : 0 · 2 5 mass % or less of at least one of the following Partially avoided impurities; and the following steps are carried out in sequence: a melting step of melting the aluminum alloy, a dehydrogenation step of removing hydrogen from the melted alloy, and removing the inclusions from the alloy after removal of hydrogen^ Casting an aluminum alloy from which inclusions are removed into an ingot; cutting the ingot to produce an aluminum cutting step having a predetermined thickness, and holding the aluminum alloy thick plate having a predetermined thickness at 200 ° C or higher for 1 hour or longer The heat treatment step of the heat treatment according to any one of claims 15 to 18, wherein the surface smoothing treatment step in the heat treatment step is performed to smooth the surface of the aluminum alloy thick plate deal with. 20. The aluminum alloy method according to the ninth aspect of the invention, wherein the surface smoothing treatment is performed by one or more selected from the group consisting of a cutting method and a honing method. [Claim 21] The method for manufacturing an alloy thick plate according to any one of claims 15 to 18, wherein a central portion of the cutting step is removed from the ingot; and the thickness direction is from a center in a thickness direction toward a surface in a thickness direction. It has the same, Μη: 0.8% by volume, Α1 and undreamable, g step, gold plate dicing 3 50 °C. In the case of the aluminum described in the section, the thickness of the central portion, the thickness of the thickness, and -109-200900512, the thickness of the ingot is τ, and the total thickness of the ingot is τ. It has a thickness of T/30 to T/5. An aluminum alloy thick plate characterized by being an aluminum alloy thick plate as described in any one of claims 1 to 4, 8 to 11 and 15 to 18. The aluminum alloy thick plate produced by the manufacturing method has an average crystal grain size of 400 k / m or less. -110-
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114574737A (en) * 2020-12-01 2022-06-03 中国科学院金属研究所 High-strength high-plasticity stress corrosion resistant nano-structure aluminum alloy and preparation method thereof

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4410835B2 (en) * 2008-03-28 2010-02-03 株式会社神戸製鋼所 Aluminum alloy thick plate and manufacturing method thereof
US10513766B2 (en) 2015-12-18 2019-12-24 Novelis Inc. High strength 6XXX aluminum alloys and methods of making the same
BR112017021504B1 (en) 2015-12-18 2022-04-05 Novelis Inc Method for producing aluminum alloy metal product, aluminum alloy metal product, transportation and automotive body parts, electronic device housing, and aluminum alloy
US11124862B2 (en) * 2017-03-03 2021-09-21 Uacj Corporation Aluminum alloy thick plate
US11932928B2 (en) 2018-05-15 2024-03-19 Novelis Inc. High strength 6xxx and 7xxx aluminum alloys and methods of making the same
TWI830452B (en) 2022-10-21 2024-01-21 財團法人工業技術研究院 Aluminum alloy material, aluminum alloy object and method for manufacturing the same

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0639664B2 (en) * 1989-08-24 1994-05-25 日本軽金属株式会社 Manufacturing method of aluminum alloy material for laser mirror
US5489363A (en) † 1993-05-04 1996-02-06 Kamyr, Inc. Pulping with low dissolved solids for improved pulp strength
JP3552577B2 (en) 1999-03-16 2004-08-11 日本軽金属株式会社 Aluminum alloy piston excellent in high temperature fatigue strength and wear resistance and method of manufacturing the same
JP2002146447A (en) 2000-11-01 2002-05-22 Daido Steel Co Ltd Degassing equipment for non-ferrous metals
US20050006010A1 (en) † 2002-06-24 2005-01-13 Rinze Benedictus Method for producing a high strength Al-Zn-Mg-Cu alloy
WO2004085096A1 (en) * 2003-03-26 2004-10-07 Showa Denko K.K. Horizontally continuously cast rod of aluminum alloy and method and equipment for producing the rod.
JP4278052B2 (en) 2003-03-26 2009-06-10 昭和電工株式会社 Aluminum alloy horizontal continuous casting rod manufacturing method
JP4214840B2 (en) * 2003-06-06 2009-01-28 住友金属工業株式会社 High-strength steel sheet and manufacturing method thereof
JP2005344173A (en) 2004-06-03 2005-12-15 Kobe Steel Ltd Aluminum-alloy substrate for magnetic disk, and its manufacturing method
JP2007051310A (en) * 2005-08-15 2007-03-01 Furukawa Sky Kk Aluminum alloy plate for aluminum bottle can body and manufacturing method thereof
JP4515363B2 (en) * 2005-09-15 2010-07-28 株式会社神戸製鋼所 Aluminum alloy plate excellent in formability and method for producing the same
JP4955969B2 (en) * 2005-09-16 2012-06-20 株式会社神戸製鋼所 Manufacturing method of forming aluminum alloy sheet
KR20080109938A (en) † 2006-05-18 2008-12-17 가부시키가이샤 고베 세이코쇼 Manufacturing Method of Aluminum Alloy Plate and Aluminum Alloy Plate
CN100478476C (en) * 2006-07-14 2009-04-15 中国铝业股份有限公司 High strength aluminium alloy wire and rod and their prepn process

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114574737A (en) * 2020-12-01 2022-06-03 中国科学院金属研究所 High-strength high-plasticity stress corrosion resistant nano-structure aluminum alloy and preparation method thereof

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