JPH04268054A - Manufacture of al-mg alloy sheet excellent in strength and orientation property - Google Patents
Manufacture of al-mg alloy sheet excellent in strength and orientation propertyInfo
- Publication number
- JPH04268054A JPH04268054A JP4758391A JP4758391A JPH04268054A JP H04268054 A JPH04268054 A JP H04268054A JP 4758391 A JP4758391 A JP 4758391A JP 4758391 A JP4758391 A JP 4758391A JP H04268054 A JPH04268054 A JP H04268054A
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- JP
- Japan
- Prior art keywords
- strength
- alloy
- subjected
- rolling
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 229910000861 Mg alloy Inorganic materials 0.000 title description 2
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 23
- 239000000956 alloy Substances 0.000 claims abstract description 23
- 229910018134 Al-Mg Inorganic materials 0.000 claims abstract description 12
- 229910018467 Al—Mg Inorganic materials 0.000 claims abstract description 12
- 238000000137 annealing Methods 0.000 claims abstract description 12
- 238000005096 rolling process Methods 0.000 claims abstract description 10
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 238000005098 hot rolling Methods 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 238000012545 processing Methods 0.000 claims description 14
- 238000000265 homogenisation Methods 0.000 claims description 5
- 230000006641 stabilisation Effects 0.000 claims description 3
- 238000011105 stabilization Methods 0.000 claims description 3
- 239000000463 material Substances 0.000 abstract description 16
- 238000000034 method Methods 0.000 abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 4
- 230000007547 defect Effects 0.000 abstract description 4
- 230000000087 stabilizing effect Effects 0.000 abstract description 2
- 238000007788 roughening Methods 0.000 abstract 1
- 229910000838 Al alloy Inorganic materials 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 239000013078 crystal Substances 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000005097 cold rolling Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 206010040925 Skin striae Diseases 0.000 description 1
- 208000031439 Striae Distensae Diseases 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 239000000523 sample Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明はアルミニウム合金板の製
造方法に係り、更に詳しくは、強度及び方向性に優れる
成形加工用Ａｌ−Ｍｇ系合金板の製造方法に関するもの
である。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an aluminum alloy plate, and more particularly to a method for producing an Al-Mg alloy plate for forming, which has excellent strength and directionality.
【０００２】0002
【従来の技術及び発明が解決しようとする課題】一般に
製造されるＰＰ（ｐｉｌｆｅｒ−ｐｒｏｏｆ）キヤップ
等のアルミニウム材料としては、純アルミニウム系の１
２００合金が使用されるているが、最近では、薄肉化の
ための高強度材が要望されてきている。[Prior Art and Problems to be Solved by the Invention] As aluminum materials for commonly manufactured PP (pilfer-proof) caps, pure aluminum
200 alloy is currently used, but recently there has been a demand for high-strength materials for thinner walls.
【０００３】高強度化のためには、■冷間加工率を上げ
た半硬質材、■Ｍｇ等の合金元素を添加した３１０５合
金（０．６％Ｍｇ）系や３００３合金（１．０％Ｍｎ）
系の硬質材が使用されている。[0003] In order to increase the strength, it is necessary to use (1) semi-hard materials with increased cold working rate, (2) 3105 alloy (0.6% Mg) series and 3003 alloy (1.0%) with alloying elements such as Mg added. Mn)
A type of hard material is used.
【０００４】しかし、１２００合金の半硬質では強度が
不足するという問題があり、３１０５合金では方向性の
バラツキが大きく、絞り加工後のトリミングを多くする
必要があり、歩留まりが低いという問題があった。また
、３００３合金系のＡｌ−Ｍｎ合金では絞り加工性が悪
い等の問題があった。However, the semi-hard 1200 alloy has a problem of insufficient strength, and the 3105 alloy has large directional variations, requires a lot of trimming after drawing, and has a low yield. . Further, the 3003 alloy type Al-Mn alloy has problems such as poor drawing workability.
【０００５】本発明は、上記従来技術の欠点を解決する
ためになされたものであって、特にＡｌ−Ｍｇ系合金に
おいて方向性、強度、成形性を併せて改善したＰＰキャ
ップ等の絞り加工に適したアルミニウム合金板の製造方
法を提供することを目的とするものである。The present invention has been made to solve the above-mentioned drawbacks of the prior art, and is particularly suitable for drawing processing of PP caps, etc., which have improved directionality, strength, and formability in Al-Mg alloys. The object of the present invention is to provide a method for manufacturing a suitable aluminum alloy plate.
【０００６】[0006]
【課題を解決するための手段】前記の課題を解決するた
め、本発明者等は、Ｍｇ量の影響、組織制御、工業的製
造方法の観点により鋭意研究開発を行った結果、合金組
成の最適化と製造条件の最適化とにより、ここに、強度
かつ方向性に優れる成形加工用Ａｌ−Ｍｇ合金板の製造
方法を開発したのである。[Means for Solving the Problems] In order to solve the above problems, the present inventors have conducted intensive research and development from the viewpoints of the influence of Mg content, microstructure control, and industrial manufacturing methods, and as a result, have found an optimal alloy composition. By optimizing the manufacturing conditions and manufacturing conditions, we have developed a method for manufacturing an Al-Mg alloy plate for forming that has excellent strength and directionality.
【０００７】すなわち、本発明は、Ｍｇ：０．５〜１．
８％、Ｍｎ：０．０５〜０．６％及びＣｕ：０．３〜０
．６％を必須成分として含有し、残部がＡｌ及び不純物
からなる組成のＡｌ−Ｍｇ系合金の鋳塊に、４５０〜５
６０℃で均質化熱処理を行い、２５０〜５５０℃の温度
で熱間圧延を行った後、加工率３０％以上の中間圧延を
行い、４２０〜５５０℃の温度で中間焼鈍を施し、更に
加工率３０％以上の仕上圧延と、１５０〜２５０℃の温
度で安定化焼鈍を施すことを特徴とする強度かつ方向性
に優れる成形加工用Ａｌ−Ｍｇ系合金板の製造方法を要
旨とするものである。That is, in the present invention, Mg: 0.5 to 1.
8%, Mn: 0.05-0.6% and Cu: 0.3-0
．． 6% as an essential component, and the remainder consists of Al and impurities.
After homogenizing heat treatment at 60°C and hot rolling at a temperature of 250 to 550°C, intermediate rolling at a processing rate of 30% or more, intermediate annealing at a temperature of 420 to 550°C, and further processing at a processing rate of 30% or more. The gist of this invention is a method for producing an Al-Mg alloy plate for forming processing, which has excellent strength and directionality, and is characterized by finishing rolling at a rate of 30% or more and stabilizing annealing at a temperature of 150 to 250°C. .
【０００８】以下に本発明を更に詳述する。The present invention will be explained in more detail below.
【０００９】[0009]
【作用】まず、本発明における合金の化学成分の限定理
由について説明する。[Operation] First, the reasons for limiting the chemical composition of the alloy in the present invention will be explained.
【００１０】Ｍｇ：
Ｍｇは固溶体強化による強度を付加するもので、本発明
が対象とするＡｌ合金はＭｇを０．５〜１．８％含有す
るＡｌ−Ｍｇ系合金である。本系合金の強度はＭｇ量と
冷間加工により導入された転位量により決定されるので
、所定量のＭｇを必須成分とする必要がある。すなわち
、Ｍｇ量が０．５％未満では材料の十分な強度が得られ
ず、一方、Ｍｇ量が１．８％を超えると、絞り加工時に
コーナー部等にストレッチヤー・ストレインマーク等の
表面欠陥や割れが発生し易くなる。したがって、Ｍｇ量
は０．５〜１．８％の範囲とする。Mg: Mg adds strength through solid solution strengthening, and the Al alloy targeted by the present invention is an Al-Mg alloy containing 0.5 to 1.8% Mg. Since the strength of this alloy is determined by the amount of Mg and the amount of dislocations introduced by cold working, it is necessary to include a predetermined amount of Mg as an essential component. In other words, if the Mg content is less than 0.5%, the material will not have sufficient strength, while if the Mg content exceeds 1.8%, surface defects such as stretch marks and strain marks may occur at corners during drawing. and cracks are more likely to occur. Therefore, the Mg amount is in the range of 0.5 to 1.8%.
【００１１】Ｃｕ：
Ｃｕは固溶体強化或いはＡｌとの析出粒子θ′−ＣｕＡ
ｌ２、Ｓ′−ＣｕＭｇＡｌ２の生成により、強度をもた
らす元素である。このために本系合金では０．３％以上
が必要である。しかし、０．６％を超えると耐食性を損
ねるので好ましくない。したがって、Ｃｕ量は０．３〜
０．６％の範囲とする。Cu: Cu is solid solution strengthened or precipitated particles θ'-CuA with Al.
It is an element that provides strength by forming 12, S'-CuMgAl2. For this reason, the present alloy requires a content of 0.3% or more. However, if it exceeds 0.6%, corrosion resistance will be impaired, which is not preferable. Therefore, the amount of Cu is 0.3~
The range is 0.6%.
【００１２】Ｍｎ：
Ｍｎは０．０５％以上含有すると、固溶体強化による材
料の強化とＭｎＡｌ６粒子による微細組織を付与する効
果があるが、０．６％を超えると晶出物による成形性の
低下や方向性が高くなるので、Ｍｎ量は０．０５〜０．
６％の範囲とする。Mn: When Mn is contained in an amount of 0.05% or more, it has the effect of strengthening the material through solid solution strengthening and imparting a fine structure due to MnAl6 particles, but when it exceeds 0.6%, formability is reduced due to crystallized substances. The amount of Mn is 0.05 to 0.0.
The range shall be 6%.
【００１３】なお、不純物は本発明の効果を損わない限
度で許容される。例えば、Ａｌ地金中に含まれるＳｉ、
Ｆｅ等の不純物が多くなると晶出物が多くなり、成形性
や耐食性を劣化させるので、Ｓｉは０．３％以下、Ｆｅ
は０．５％以下に規制するのが望ましい。またＴｉは０
．０５％以下が望ましい。[0013] Impurities are allowed within limits that do not impair the effects of the present invention. For example, Si contained in Al ingot,
If impurities such as Fe increase, the amount of crystallized substances will increase, deteriorating formability and corrosion resistance, so Si should be 0.3% or less and Fe
It is desirable to regulate it to 0.5% or less. Also, Ti is 0
．． 0.05% or less is desirable.
【００１４】次に、上記Ａｌ−Ｍｇ系合金板の製造方法
について説明する。Next, a method for manufacturing the above-mentioned Al--Mg alloy plate will be explained.
【００１５】上記化学成分を有するアルミニウム合金を
鋳造して得られた鋳塊は内部に不均質に分布している主
要元素の均質化及び遷移元素とＡｌとの金属間化合物Ｍ
ｎＡｌ６を生成させた後、熱間圧延を行う必要がある。
したがって、均質化熱処理は４５０〜５６０℃の温度で
行うのが好ましい。[0015] The ingot obtained by casting an aluminum alloy having the above chemical composition has homogenization of the main elements which are heterogeneously distributed inside, and an intermetallic compound M of transition elements and Al.
After generating nAl6, it is necessary to perform hot rolling. Therefore, the homogenization heat treatment is preferably performed at a temperature of 450 to 560°C.
【００１６】均質化熱処理後、２５０〜５５０℃の温度
で熱間圧延を行い、粗い鋳塊組織を展伸材組織に加工す
る。これにより、上記の金属間化合物が結晶粒の粗大化
を阻止し、未再結晶粒組織か細かい再結晶組織が付与さ
れる。なお、熱間圧延後に中間焼鈍を施してもよく、中
間焼鈍を施すと、より材料組織の制御が容易となる。[0016] After the homogenization heat treatment, hot rolling is performed at a temperature of 250 to 550°C to process the rough ingot structure into a wrought material structure. As a result, the above-mentioned intermetallic compound prevents coarsening of crystal grains, and a non-recrystallized grain structure or a fine recrystallized grain structure is provided. Note that intermediate annealing may be performed after hot rolling, and the material structure can be more easily controlled by performing intermediate annealing.
【００１７】次いで、加工率３０％以上の中間圧延（冷
間圧延）を施す。加工率が３０％未満の圧延では最終的
な結晶粒が４０μｍよりも大きくなり、成形加工時に肌
荒れとなり、表面品質を損ねるので好ましくない。[0017] Next, intermediate rolling (cold rolling) is performed at a processing rate of 30% or more. Rolling with a processing rate of less than 30% is not preferred because the final crystal grains will be larger than 40 μm, resulting in rough skin during forming and impairing surface quality.
【００１８】その後、中間焼鈍を施すが、加熱温度が４
２０℃未満ではＭｇ、Ｃｕ、Ｍｎの十分な固溶、並びに
低耳材に必要な十分な立方方位の再結晶材が得られない
。
一方、５５０℃を超えると結晶粒の粗大化、バーニング
の危険性がある。したがって、中間焼鈍の温度は４２０
〜５５０℃の範囲とする。なお、保持時間は１〜１０秒
で十分である。[0018] After that, intermediate annealing is performed, but the heating temperature is 4.
If the temperature is lower than 20° C., sufficient solid solution of Mg, Cu, and Mn and sufficient cubic-oriented recrystallized material necessary for a low-edge material cannot be obtained. On the other hand, if the temperature exceeds 550°C, there is a risk of coarsening of crystal grains and burning. Therefore, the temperature of intermediate annealing is 420
The temperature should be in the range of ~550°C. Note that a holding time of 1 to 10 seconds is sufficient.
【００１９】続く最終的な仕上圧延（冷間圧延）は、３
０％以上の加工率で行う。加工率が３０％未満では十分
な強度が得られない。なお、本発明の場合、あまり加工
率を高くしなくとも高強度が得られるので、低耳材の観
点からも加工率は５０％以下にとどめるのが製造上望ま
しい。The subsequent final finish rolling (cold rolling) is carried out at 3
Perform at a processing rate of 0% or more. If the processing rate is less than 30%, sufficient strength cannot be obtained. In the case of the present invention, high strength can be obtained without increasing the processing rate too much, so it is desirable for manufacturing to keep the processing rate to 50% or less from the viewpoint of low selvage material.
【００２０】最後に１５０〜２５０℃の温度で安定化焼
鈍を施す。この場合、１５０℃未満では内部組織の変化
を起こすのに不十分であり、また２５０℃を超えると軟
化が進んで十分な強度が得られない。この安定化焼鈍に
より、成形材に必要な伸びの回復と固溶状態にあったＭ
ｇ原子は安定存在状態になり、絞り加工時にＳＳマーク
の発生が抑制される。Finally, stabilization annealing is performed at a temperature of 150 to 250°C. In this case, if it is less than 150°C, it is insufficient to cause changes in the internal structure, and if it exceeds 250°C, softening progresses and sufficient strength cannot be obtained. This stabilization annealing restores the elongation necessary for the formed material and M
The g atoms enter a stable state of existence, and the generation of SS marks during drawing is suppressed.
【００２１】以上の方法で得られるＡｌ−Ｍｇ系合金板
において、結晶粒度が４０μｍを超えると絞り加工時に
肌荒れを起こし、また１０μｍ未満であるとＳＳマーク
が発生し易くなる。したがって、結晶粒度は１０〜４０
μｍの範囲に調整するのが好ましい。In the Al-Mg alloy plate obtained by the above method, if the grain size exceeds 40 μm, surface roughness occurs during drawing, and if it is less than 10 μm, SS marks are likely to occur. Therefore, the grain size is 10-40
It is preferable to adjust it to a range of μm.
【００２２】なお、このようにして得られたＡｌ−Ｍｇ
系合金板は常法による成形加工によってＰＰキャップ等
に加工されるが、成形品はＳＳマーク発生がなく強度、
方向性が優れている。[0022] Furthermore, the Al-Mg obtained in this way
The alloy sheet is processed into PP caps, etc. by conventional molding processes, but the molded products do not generate SS marks and have good strength and
Excellent direction.
【００２３】次に本発明の実施例を示す。Next, examples of the present invention will be shown.
【００２４】[0024]
【表１】
に示す化学成分を有するＡｌ合金の鋳塊（厚さ５０ｍｍ
）を面削し、５００℃×８ｈｒの均質化熱処理を施した
後、３００〜５００℃の温度で熱間圧延を行い、厚さ２
〜４ｍｍの熱間圧延板とした。[Table 1] Al alloy ingot (thickness: 50 mm) having the chemical composition shown in
) was subjected to homogenization heat treatment at 500°C x 8 hours, then hot rolled at a temperature of 300 to 500°C to a thickness of 2
It was made into a hot rolled plate of ~4 mm.
【００２５】その後、[0025] After that,
【表２】
に示す条件で加工、熱処理を施して厚さ０．２３ｍｍの
供試材を得た。得られた供試材について結晶粒度を調べ
ると共に、引張特性、表面状況（ＳＳマーク）、耳率（
方向性）及び肌荒れ状況を調査した。その結果を表２に
併記する。なお、耳率及びＳＳマークは４０ｍｍφポン
チ、ブランク径６６．７ｍｍφ（絞り率４０％）にて測
定した。[Table 2] Processing and heat treatment were performed under the conditions shown in Table 2 to obtain a test material with a thickness of 0.23 mm. In addition to examining the crystal grain size of the obtained sample material, the tensile properties, surface condition (SS mark), and selvedge ratio (
direction) and the condition of rough skin. The results are also listed in Table 2. Note that the selvage ratio and the SS mark were measured using a 40 mmφ punch and a blank diameter of 66.7 mmφ (reduction rate of 40%).
【００２６】表２において、本発明例はいずれも、所望
の高強度が得られると共に、ＳＳマークや肌荒れ等の表
面欠陥がなく、良好な成形材が得られていることがわか
る。一方、比較例のものは、たとえ高強度が得られても
、ＳＳマーク、耳率、肌荒れ等でいずれも満足できない
。In Table 2, it can be seen that in all of the examples of the present invention, desired high strength was obtained, and there were no surface defects such as SS marks or rough skin, and good molded materials were obtained. On the other hand, the comparative examples, even if high strength is obtained, are unsatisfactory in terms of SS mark, selvage rate, rough skin, etc.
【００２７】[0027]
【発明の効果】以上詳述したように、本発明によれば、
Ｍｇ量が１．８％以下の特定組成のＡｌ−Ｍｇ系合金に
特定条件の圧延加工、熱処理を施すので、成形時にＳＳ
マークや肌荒れ等の表面欠陥がなく、低耳の高強度アル
ミニウム材料を得ることができ、強度かつ方向性に優れ
たＰＰキャップ等を製造することが可能である。また、
本発明法によれば工業的製造が容易である。[Effects of the Invention] As detailed above, according to the present invention,
Since the Al-Mg alloy with a specific composition with an Mg content of 1.8% or less is subjected to rolling processing and heat treatment under specific conditions, SS is maintained during forming.
It is possible to obtain a high-strength aluminum material with a low profile and no surface defects such as marks or roughness, and it is possible to manufacture PP caps and the like with excellent strength and directionality. Also,
According to the method of the present invention, industrial production is easy.
Claims (1)
５〜１．８％、Ｍｎ：０．０５〜０．６％及びＣｕ：０
．３〜０．６％を必須成分として含有し、残部がＡｌ及
び不純物からなる組成のＡｌ−Ｍｇ系合金の鋳塊に、４
５０〜５６０℃で均質化熱処理を行い、２５０〜５５０
℃の温度で熱間圧延を行った後、加工率３０％以上の中
間圧延を行い、４２０〜５５０℃の温度で中間焼鈍を施
し、更に加工率３０％以上の仕上圧延と、１５０〜２５
０℃の温度で安定化焼鈍を施すことを特徴とする強度か
つ方向性に優れる成形加工用Ａｌ−Ｍｇ系合金板の製造
方法。Claim 1: In weight % (the same applies hereinafter), Mg: 0.
5-1.8%, Mn: 0.05-0.6% and Cu: 0
．． An ingot of an Al-Mg alloy containing 3 to 0.6% as an essential component, with the remainder consisting of Al and impurities,
Homogenization heat treatment at 50-560℃, 250-550℃
After hot rolling at a temperature of 30% or more, intermediate rolling is performed at a working rate of 30% or more, intermediate annealing is performed at a temperature of 420 to 550°C, and further finish rolling is performed at a working rate of 30% or more, and 150 to 250° C.
A method for producing an Al-Mg alloy plate for forming processing, which is characterized by performing stabilization annealing at a temperature of 0° C. and has excellent strength and directionality.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4758391A JPH04268054A (en) | 1991-02-20 | 1991-02-20 | Manufacture of al-mg alloy sheet excellent in strength and orientation property |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4758391A JPH04268054A (en) | 1991-02-20 | 1991-02-20 | Manufacture of al-mg alloy sheet excellent in strength and orientation property |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04268054A true JPH04268054A (en) | 1992-09-24 |
Family
ID=12779278
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4758391A Pending JPH04268054A (en) | 1991-02-20 | 1991-02-20 | Manufacture of al-mg alloy sheet excellent in strength and orientation property |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04268054A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003327262A (en) * | 2002-03-07 | 2003-11-19 | Mitsubishi Materials Corp | Caps and bottle cans and screw-type sealed bottles |
| JP2007092151A (en) * | 2005-09-29 | 2007-04-12 | Furukawa Sky Kk | Aluminum alloy for cap and method for producing the same |
| CN104694801A (en) * | 2015-03-20 | 2015-06-10 | 东北轻合金有限责任公司 | Al-Mg-Sc-Zr aluminum alloy plate and manufacturing method thereof |
| CN104818412A (en) * | 2015-05-27 | 2015-08-05 | 东北轻合金有限责任公司 | Low-Sc Al-Mg-Sc-Zr alloy sheet and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52105509A (en) * | 1976-03-03 | 1977-09-05 | Mitsubishi Aluminium | Production of aluminium alloy sheet for deep drawing |
| JPH02290953A (en) * | 1989-04-29 | 1990-11-30 | Kobe Steel Ltd | Production of al-mg alloy free from occurrence of stretcher strain mark at the time of forming |
-
1991
- 1991-02-20 JP JP4758391A patent/JPH04268054A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS52105509A (en) * | 1976-03-03 | 1977-09-05 | Mitsubishi Aluminium | Production of aluminium alloy sheet for deep drawing |
| JPH02290953A (en) * | 1989-04-29 | 1990-11-30 | Kobe Steel Ltd | Production of al-mg alloy free from occurrence of stretcher strain mark at the time of forming |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003327262A (en) * | 2002-03-07 | 2003-11-19 | Mitsubishi Materials Corp | Caps and bottle cans and screw-type sealed bottles |
| JP2007092151A (en) * | 2005-09-29 | 2007-04-12 | Furukawa Sky Kk | Aluminum alloy for cap and method for producing the same |
| CN104694801A (en) * | 2015-03-20 | 2015-06-10 | 东北轻合金有限责任公司 | Al-Mg-Sc-Zr aluminum alloy plate and manufacturing method thereof |
| CN104818412A (en) * | 2015-05-27 | 2015-08-05 | 东北轻合金有限责任公司 | Low-Sc Al-Mg-Sc-Zr alloy sheet and preparation method thereof |
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