JPH0441678A - Aluminum alloy material having superior corrosion resistance - Google Patents
Aluminum alloy material having superior corrosion resistanceInfo
- Publication number
- JPH0441678A JPH0441678A JP14723990A JP14723990A JPH0441678A JP H0441678 A JPH0441678 A JP H0441678A JP 14723990 A JP14723990 A JP 14723990A JP 14723990 A JP14723990 A JP 14723990A JP H0441678 A JPH0441678 A JP H0441678A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- alloy material
- corrosion resistance
- surface layer
- difference
- 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.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 39
- 239000000956 alloy Substances 0.000 title claims abstract description 35
- 238000005260 corrosion Methods 0.000 title claims abstract description 27
- 230000007797 corrosion Effects 0.000 title claims abstract description 26
- 239000002344 surface layer Substances 0.000 claims abstract description 18
- 238000005219 brazing Methods 0.000 claims abstract description 13
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 10
- 239000000463 material Substances 0.000 claims description 11
- 239000006104 solid solution Substances 0.000 claims description 11
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 4
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 claims description 3
- 239000000243 solution Substances 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 150000002222 fluorine compounds Chemical class 0.000 claims 1
- 229910001635 magnesium fluoride Inorganic materials 0.000 abstract description 8
- 239000010410 layer Substances 0.000 abstract description 7
- 238000010438 heat treatment Methods 0.000 abstract description 6
- 239000000498 cooling water Substances 0.000 abstract description 4
- 229910052731 fluorine Inorganic materials 0.000 abstract description 4
- 229910045601 alloy Inorganic materials 0.000 abstract description 3
- 239000011737 fluorine Substances 0.000 abstract description 2
- 239000011159 matrix material Substances 0.000 abstract description 2
- 239000007787 solid Substances 0.000 abstract 3
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 abstract 1
- 229910017708 MgZn2 Inorganic materials 0.000 abstract 1
- 230000035515 penetration Effects 0.000 abstract 1
- 239000011162 core material Substances 0.000 description 9
- 239000010405 anode material Substances 0.000 description 7
- 238000005253 cladding Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000945 filler Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000007747 plating Methods 0.000 description 3
- 229910017706 MgZn Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 150000002500 ions Chemical class 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 108091006629 SLC13A2 Proteins 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- -1 fluorine ions Chemical class 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
Landscapes
- Chemical Treatment Of Metals (AREA)
Abstract
Description
本発明は、耐食性に優れたアルミニウム合金材、特に冷
却水側の耐食性に優れた特性を要求される熱交換器用の
チューブに用いられるアルミニウム合金材に関するもの
である。The present invention relates to an aluminum alloy material with excellent corrosion resistance, particularly an aluminum alloy material used for tubes for heat exchangers that require excellent corrosion resistance on the cooling water side.
ラジェータチューブ用のアルミニウム合金プレージング
シートとしては、例えば特開昭６２−２２７０５６号公
報にも示されているように、＾１−Ｍｎ−Ｃｕ系合金を
芯材とし、この芯材の片面に＾１−５ｉ系または＾にＳ
１−Ｍｇ系のろう材を、又、もう−方の片面に犠牲陽極
材として＾ｌ−Ｍｇ−Ｚｎ系合金を各々１０％程度の厚
さでクラッドした、いわゆる３層構造のプレージングシ
ートが使用されている。
ところで、近年、燃費などの点からもラジェータの軽量
化に対する要請は高く、従ってラジェータのチューブ材
料の薄肉化は避けることができなくなりつつある。
しかしながら、ラジェータのチューブの耐食性は当然の
こととして要求されており、チューブ内面（冷却水側）
の防食対策は前記クラッドした犠牲陽極材により実施さ
れている訳であるが、チューブ材を薄肉化する場合にあ
っては、クラツド率を従来通りとすると、犠牲陽極材の
絶対厚さが小さくなる為、ＣｕやＭｎの濃度勾配が小さ
くなり、防食機能が失われてしまう。
尚、濃度勾配を確保する為にクラツド率を高くすると、
チューブ材の厚さに占める犠牲陽極材の厚さの割合が大
きくなり、チューブ全体としての強度低−下は逸れ得す
、しかもチューブ材の厚さに占める犠牲陽極層の割合が
大きくなり、チューブ材に対して腐食深さが深くなり、
貫通孔が形成され易い問題が有る。As an aluminum alloy plating sheet for a radiator tube, for example, as shown in JP-A-62-227056, a ^1-Mn-Cu alloy is used as a core material, and one side of this core material is ^1-Mn-Cu based alloy. 1-5i series or ^S
A so-called three-layer plating sheet is clad with 1-Mg-based brazing filler metal and 1-Mg-Zn-based alloy as a sacrificial anode material on the other side, each with a thickness of about 10%. It is used. Incidentally, in recent years, there has been a strong demand for reducing the weight of radiators from the viewpoint of fuel efficiency, etc. Therefore, it is becoming impossible to avoid reducing the thickness of the tube material of the radiator. However, corrosion resistance is naturally required for radiator tubes, and the inner surface of the tube (cooling water side)
The anti-corrosion measure is implemented by using the clad sacrificial anode material, but when making the tube material thinner, if the cladding ratio remains the same as before, the absolute thickness of the sacrificial anode material will become smaller. Therefore, the concentration gradient of Cu and Mn becomes small, and the anticorrosion function is lost. In addition, if the cladding ratio is increased to ensure a concentration gradient,
The ratio of the thickness of the sacrificial anode layer to the thickness of the tube material increases, and the strength of the tube as a whole may decrease.Furthermore, the ratio of the sacrificial anode layer to the thickness of the tube material increases, causing The corrosion depth becomes deeper in the material,
There is a problem that through holes are easily formed.
本発明の第１の目的は、薄肉化しても耐食性に優れたア
ルミニウム合金材を提供することである。
本発明の第２の目的は、薄肉化しても強度特性が満足で
きるアルミニウム合金材を提供することである。
上記本発明の目的は、０．０５〜０．６％のＭｇ及び０
．２〜１．０％のＺｎを含有するアルミニウム合金材で
あって、このアルミニウム合金材の表層にはＭｇＦ２が
生成し、表層と深部との間でＺｎ固溶量に差が形成され
て電位勾配が構成されてなることを特徴とする耐食性に
優れたアルミニウム合金材によって達成される。
尚、このアルミニウム合金材は、例えば熱交換器用のチ
ューブに用いる為、アルミニウム合金材の一面の表層に
はＭｇＦ２が生成し、表層と深部との一間でＺｒｒ固溶
量に差が形成されて電位勾配が構成され、かつ、アルミ
ニウム合金材の他面にはろう材がクラッドされてなるも
のが好ましく、そしてアルミニウム合金材の一面にフッ
素化合物又はフッ素イオン含有溶液を介在させ、熱処理
することてその表層にはＭｇＦ２が生成し、表層と深部
との間でＺｎ固溶量に差が形成されて電位勾配は構成さ
れてなり、又、アルミニウム合金材としては、０．０５
〜０．６％のＭｇ及び０．２〜１．０％のＺｎを含有す
るだけではなく、さらに０．１〜１．５％のＨｎ、０．
３〜１．２％のＳｉ、０．３〜１．．５％のＦｅ、０．
０５〜０．２０％のＣｕ、及び０．０５〜０１５％のＺ
ｒの群の中から選ばれる一種又は二種以上のものが含有
され、残りがＡｌと不可避不純物とからなる組成のもの
が好ましい。
ところで、本発明は次の技術思想が総合的に勘案されて
達成されたものである。
すなわち、
■ Ｚｎは＾１素地中に固溶すると、電位を卑にする傾
向がある。
■ ＺｎはＭｇと共に＾１素地中に含有されて、溶体化
処理されると、その後の時効処理によりＭＨ２ｎ２とし
て析出する。
このＭｇＺｎ ２におけるＺｎは、電位に影響を及ぼさ
ない。
■ ＭｇはＦと反応し易＜、ＭｇＦ２を生成する。
といっな技術思想を総合的に組み立てることにより、犠
牲陽極材をクラッドしなくても、芯材内に電位勾配を付
与することが出来ることを見出し、これによって本発明
が完成されたのである。
つまり、第１図（ａ）に示す如＜、Ｍｇ及びＺｎを含有
するアルミニウム合金の面にＦを存在させ、そしてろう
付は加熱といった熱処理を施すと、第１［Ｊ（ｂ）に示
される如く、表面近傍ではＦの侵食によってＭｇＦ２が
形成され、Ｚｎは＾１素地中に固溶し、又、深部ではＭ
ｇとＺｎがＨｇＺｎ ２として析出する。
従って、表面近傍と深部との間ではＺｎ固溶量に差が出
来、この差によって電位勾配が構成され、これが犠牲陽
極層となり、耐食性に富むものとなるのである。そして
、この犠牲陽極層が構成された側の面がチューブの内面
側となるように構成させれば、冷却水に対して耐食性に
優れた熱交換器用のチューブが得られることになる。
ここで、Ｆの介在は、フッ化物を塗布しても良く、ある
いはフッ素イオンを含む溶液中に浸漬して＾１の酸化皮
膜中にＦを含浸させてもよく、その他適宜な手段を採用
できる。
尚、電位勾配の大きさく高低差）は、熱処理前における
表面のＦ量に依存するから、防食性に応じて適宜な量を
設定すれば良いが、大体０，２〜３．０ｇ ／ ｍ ２
の量のＦが表面に存在するようにすれば十分である。
このように犠牲陽極材をクラッドしなくても耐食性が確
保される為に、アルミニウム合金材は芯材とろう材の２
層クラッドでよく、３層クラッドに比べてコストが低廉
なものともなる。
尚、本発明において、アルミニウム合金材の組成として
Ｍｇ及びＺｎが必須成分とされているのは、次の理由に
基づく。
すなわち、アルミニウム合金材深部では、ろう付けとい
った熱処理後にＭｇＺｎ、とじて析出し、表面層で、は
ｈはＦと反応して８ｇＦ２となり、ｚｎが＾Ｉ素地ψに
固溶し、°これによって電位勾配を“構成するからであ
る。
ところで、この時、阿ｇが０．０５％未満の少なすぎる
場合、又、Ｚｎが０．２０％未満の少なすぎる場合では
、所望の耐食性の効果が得られず、逆に、Ｍｇが０．６
％を超えて多すぎる場合、又、Ｚｎが１．０％を越えて
多すぎる場合では、アルミニウム合金材に粒界腐食を生
じるようになったからである。
又、アルミニウム合金材中にＭｎ、 Ｓｉ、 Ｆｅ、
Ｃｕ、Ｚｒが含まれるのが好ましいのは、次の理由に基
づく。
Ｍｎ、Ｓｉ、 Ｆｅ、 Ｚｒ等の元素は＾Ｉとの２元系
化合物を形成し、あるいは＾１−Ｍｎ−５ｉ系、−＾ｌ
−Ｍｎ−Ｆｅ系、＾１−５ｉ−Ｚｒ系、＾１−Ｍｎ−５
ｉＦｅ系等の化合物を形成して、強度向上に寄与するか
らである。
又、Ｎｎは芯材となるアルミニウム合金材の耐食性を向
上させるからである。
尚、Ｎｎが０．１％未満の少なすぎる場合、Ｓｉが０．
３％未満の少なすぎる場合、Ｆｅが０゜３％未満の少な
すぎる場合、Ｚｎが０．０５％未満の少なすぎる場合で
は効果が小さい。
又、Ｍｎが１．５％を超えて多すぎる場合には、加工性
か低下し、又、粒界腐食怒受性を高め、Ｓｉが１２％を
越えて多すぎる場合には、固相線温度が低下し、ろう付
時にろうの侵食を受けやすくなり、又、Ｆｅが１．５％
を超えて多すぎる場合には、結晶粒が微細化してろう付
時にろうの侵食を受は易くなり、又、Ｚｒが１．５％を
超えて多すぎる場合には、加工性が低下する傾向がある
。
従って、Ｍｎ、Ｓｉ、 Ｆｅ、Ｚｒ等の元素を添加する
場合にあっては、Ｍｎは０．１〜１．５％、Ｓｉは０．
３〜１．２％、Ｆｅは０．３〜１．５％、Ｚｒは０．０
５〜０．１５％であることが好ましい。
又、Ｃｕは＾１素地中に固溶して強度を高めると共に、
耐孔食性を向上させるものであるが、０．０５％未満の
少なすぎる場合には効果が少なく、逆に、０．２０％を
超えて多すぎる場合には、＃料の電位がＣｕによって支
配されるようになり、Ｚｎの固溶量差による電位勾配が
失われる傾向があるから、Ｃｕを添加する場合にあって
は０．０５〜０．２％であることが好ましい。A first object of the present invention is to provide an aluminum alloy material that has excellent corrosion resistance even when made thin. A second object of the present invention is to provide an aluminum alloy material that has satisfactory strength characteristics even when the wall thickness is reduced. The object of the present invention is to provide 0.05 to 0.6% Mg and 0.05 to 0.6% Mg and
．． This is an aluminum alloy material containing 2 to 1.0% Zn, and MgF2 is generated on the surface layer of this aluminum alloy material, and a difference in the amount of Zn solid solution is formed between the surface layer and the deep part, resulting in a potential gradient. This is achieved using an aluminum alloy material with excellent corrosion resistance. Since this aluminum alloy material is used, for example, in tubes for heat exchangers, MgF2 is generated in the surface layer of one side of the aluminum alloy material, and a difference is formed in the amount of Zrr solid solution between the surface layer and the deep part. It is preferable that a potential gradient is formed and the other surface of the aluminum alloy material is clad with a brazing filler metal. MgF2 is generated in the surface layer, and a difference in the amount of Zn solid solution is formed between the surface layer and the deep part, forming a potential gradient.
It not only contains ~0.6% Mg and 0.2-1.0% Zn, but also 0.1-1.5% Hn, 0.
3-1.2% Si, 0.3-1. ．． 5% Fe, 0.
05-0.20% Cu and 0.05-015% Z
It is preferable that the composition contains one or more selected from the group r, with the remainder consisting of Al and unavoidable impurities. By the way, the present invention has been achieved by comprehensively considering the following technical ideas. That is, (1) When Zn is dissolved in solid solution in the substrate, it tends to make the potential less noble. (2) Zn is contained in the ^1 matrix together with Mg, and when it is solution treated, it is precipitated as MH2n2 by the subsequent aging treatment. Zn in this MgZn 2 does not affect the potential. ■ Mg easily reacts with F, producing MgF2. By comprehensively assembling these technical ideas, it was discovered that a potential gradient could be applied within the core material without cladding the sacrificial anode material, and the present invention was thus completed. In other words, as shown in Fig. 1(a), if F is present on the surface of an aluminum alloy containing Mg and Zn, and heat treatment such as heating is performed for brazing, the As shown, MgF2 is formed near the surface by the erosion of F, Zn is dissolved in solid solution in the substrate, and MgF2 is formed in the deep part.
g and Zn precipitate as HgZn2. Therefore, there is a difference in the amount of solid solution of Zn between the vicinity of the surface and the deep part, and this difference forms a potential gradient, which becomes a sacrificial anode layer and has high corrosion resistance. If the surface on which the sacrificial anode layer is formed is configured to be the inner surface of the tube, a tube for a heat exchanger with excellent corrosion resistance against cooling water can be obtained. Here, the intervention of F may be achieved by applying fluoride, or by impregnating F into the oxide film of ^1 by immersing it in a solution containing fluorine ions, or any other appropriate means may be employed. . Note that the magnitude of the potential gradient (height difference) depends on the amount of F on the surface before heat treatment, so it is sufficient to set an appropriate amount depending on the corrosion resistance, but it is approximately 0.2 to 3.0 g / m 2
It is sufficient that an amount of F is present on the surface. In this way, in order to ensure corrosion resistance without cladding the sacrificial anode material, aluminum alloy material has two parts: core material and brazing material.
A layered cladding is sufficient, and the cost is lower than that of a three-layered cladding. The reason why Mg and Zn are essential components in the composition of the aluminum alloy material in the present invention is based on the following reason. That is, in the deep part of the aluminum alloy material, MgZn precipitates after heat treatment such as brazing, and in the surface layer, h reacts with F to become 8gF2, and zn is dissolved in the base material ψ, thereby increasing the potential. By the way, at this time, if Ag is too small, less than 0.05%, or if Zn is too small, less than 0.20%, the desired corrosion resistance effect cannot be obtained. On the contrary, Mg is 0.6
This is because if the Zn content exceeds 1.0%, or if the Zn content exceeds 1.0%, intergranular corrosion occurs in the aluminum alloy material. In addition, Mn, Si, Fe,
The reason why Cu and Zr are preferably included is based on the following reason. Elements such as Mn, Si, Fe, and Zr form binary compounds with ^I, or ^1-Mn-5i, -^l
-Mn-Fe system, ^1-5i-Zr system, ^1-Mn-5
This is because it forms an iFe-based compound or the like and contributes to improving strength. In addition, Nn improves the corrosion resistance of the aluminum alloy material serving as the core material. Note that if Nn is too small, less than 0.1%, Si may be 0.1%.
If the content is too low (less than 3%), if the Fe content is too low (less than 0.3%), if the Zn content is too low (less than 0.05%), the effect will be small. Furthermore, if Mn is too large (more than 1.5%), the processability will be reduced and the resistance to intergranular corrosion will be increased, and if Si is too large (more than 12%), the solidus The temperature decreases, the wax becomes more susceptible to corrosion during brazing, and the Fe content is 1.5%.
If the Zr content exceeds 1.5%, the crystal grains become finer and are more susceptible to brazing during brazing, and if the Zr content exceeds 1.5%, the workability tends to decrease. There is. Therefore, when adding elements such as Mn, Si, Fe, and Zr, Mn should be added in an amount of 0.1 to 1.5%, and Si should be added in an amount of 0.1 to 1.5%.
3-1.2%, Fe 0.3-1.5%, Zr 0.0
It is preferably 5 to 0.15%. In addition, Cu is dissolved in solid solution in the base material and increases the strength,
It improves pitting corrosion resistance, but if the amount is too small (less than 0.05%), the effect is small; on the other hand, if it is too large (more than 0.20%), the potential of the # material is dominated by Cu. Therefore, when Cu is added, it is preferably 0.05 to 0.2% since the potential gradient due to the difference in the amount of solid solution of Zn tends to be lost.
【実施例１〜１６】
表に示す組成の本発明になるアルミニウム合金材（プレ
ージングシート芯材）１〜１６を鋳造した後、通常の条
件で熱間圧延を行い、９＋ｎｍ厚の板とした。
この板にＩＩ厚のＪＩＳ ４０４５アルミニウム合金か
らなるろう材を重ね合わせて熱間圧延、冷間圧延を行い
、０．１８ｍＨ厚の冷延板とした。
そして、この後、板の表面（ろう材をクラッドしていな
い側の表面）にフッ化物系フラックスを１０ｇ／ｎ＋’
（Ｆ量としては１．５Ｂ／ｍ”）厚塗布し、ろう付けを
想定した６００℃で５分間の熱処理を施した。[Examples 1 to 16] After casting aluminum alloy materials (plating sheet core materials) 1 to 16 of the present invention having the compositions shown in the table, hot rolling was performed under normal conditions to form a plate with a thickness of 9+ nm. . A brazing filler metal made of JIS 4045 aluminum alloy having a thickness of II was superimposed on this plate, and hot rolling and cold rolling were performed to obtain a cold rolled plate having a thickness of 0.18 mH. After this, 10g/n+' of fluoride flux was applied to the surface of the plate (the surface not clad with brazing material).
It was applied thickly (F amount: 1.5 B/m") and heat-treated at 600° C. for 5 minutes, assuming brazing.
【比較例１〜５】
表に示す組成のアルミニウム合金材（プレージングシー
ト芯材）１〜５のものについて、実施例１と同様に行っ
た。[Comparative Examples 1 to 5] The same procedure as in Example 1 was conducted for aluminum alloy materials (praising sheet core materials) 1 to 5 having the compositions shown in the table.
【比較例６】
＾１−１．Ｏ４Ｍｎ −０，４７Ｃｕの芯材に＾Ｉ−０
．２２Ｚｎ−０．４４−Ｍｇからなる犠牲陽極材をクラ
ツド率１０％の割合でクラッドしてなるアルミニウム合
金板（芯材８輸−１犠牲陽極材１ ｍｍ＞のものについ
て、実施例１と同様に行った。
【特性］
上記各側で得なものについて、耐食性を評価する為、１
ｐｐＩＩのＣｕ”イオンと１ ｐｐ＋＊のＦｅ’＋イオ
ン（塩化物）とを添加した１１０００ｐｐ＋のＮａＣ１
及び５００ｐｐｍのＮａ２５ｏ、の混合溶液中に４０℃
で１ケ月間浸漬し、孔食深さを測定したので、その結果
を表に示す。
又、強度を評価する為、９０℃で２週間の処理後の引張
強さを測定したので、その結果を表に併せて示す。
この表に示される結果から判るように、本発明のものは
比較例のものに比べて耐食性が著しく優れている。
従って、例えばラジェータ用チューブに本発明の薄肉化
したアルミニウム合金材を用いても、耐久性に富むもの
である。[Comparative Example 6] ^1-1. O4Mn -0,47Cu core material ^I-0
．． An aluminum alloy plate (core material: 8 x 1 sacrificial anode material: 1 mm) clad with a sacrificial anode material made of 22Zn-0.44-Mg at a cladding ratio of 10% was prepared in the same manner as in Example 1. [Characteristics] In order to evaluate the corrosion resistance of the above-mentioned products, 1.
11000 pp+ NaC1 with ppII Cu'' ions and 1 pp+* Fe'+ ions (chloride)
and 500 ppm Na25O at 40°C.
The pitting depth was measured after soaking for one month, and the results are shown in the table. In addition, in order to evaluate the strength, the tensile strength was measured after treatment at 90°C for two weeks, and the results are also shown in the table. As can be seen from the results shown in this table, the corrosion resistance of the specimens of the present invention is significantly superior to that of the comparative examples. Therefore, even if the thinned aluminum alloy material of the present invention is used, for example, in a radiator tube, it is highly durable.
第１０図（ａ）及び（ｂ）は、 アルミニウム合金材の説 四面である。 FIGS. 10(a) and (b) are Theory of aluminum alloy materials It has four sides.
Claims (4)
のＺｎを含有するアルミニウム合金材であって、このア
ルミニウム合金材の表層にはＭｇＦ＿２が生成し、表層
と深部との間でＺｎ固溶量に差が形成されて電位勾配が
構成されてなることを特徴とする耐食性に優れたアルミ
ニウム合金材。(1) 0.05-0.6% Mg and 0.2-1.0%
An aluminum alloy material containing Zn, in which MgF_2 is generated on the surface layer of the aluminum alloy material, and a difference in the amount of Zn solid solution is formed between the surface layer and the deep part, forming a potential gradient. An aluminum alloy material with excellent corrosion resistance.
ミニウム合金材であって、アルミニウム合金材の一面の
表層にはＭｇＦ＿２が生成し、表層と深部との間でＺｎ
固溶量に差が形成されて電位勾配が構成され、かつ、ア
ルミニウム合金材の他面にはろう材が設けられてなるも
の。(2) An aluminum alloy material with excellent corrosion resistance as described in claim 1, in which MgF_2 is generated on one surface layer of the aluminum alloy material, and Zn is formed between the surface layer and the deep part.
A potential gradient is formed by forming a difference in the amount of solid solution, and a brazing material is provided on the other side of the aluminum alloy material.
優れたアルミニウム合金材であって、アルミニウム合金
材の一面にフッ素化合物又はフッ素イオン含有溶液を介
在させ、熱処理することでその表層にはＭｇＦ＿２が生
成し、表層と深部とめ間でＺｎ固溶量に差が形成されて
電位勾配が構成されてなるもの。(3) An aluminum alloy material having excellent corrosion resistance as set forth in claim 1 or 2, wherein a fluorine compound or a fluorine ion-containing solution is interposed on one surface of the aluminum alloy material, and the surface layer is heat-treated. MgF_2 is generated, and a difference in the amount of Zn solid solution is formed between the surface layer and the deep part, creating a potential gradient.
れたアルミニウム合金材であって、アルミニウム合金材
は、０．０５〜０．６％のＭｇ及び０．２〜１．０％の
Ｚｎを含有し、さらに０．１〜１．５％のＭｎ、０．３
〜１．２％のＳｉ、０．３〜１．５％のＦｅ、０．０５
〜０．２０％のＣｕ、及び０．０５〜０．１５％のＺｒ
の群の中から選ばれる一種又は二種以上のものが含有さ
れ、残りがＡｌと不可避不純物とからなる組成を有する
もの。(4) An aluminum alloy material with excellent corrosion resistance according to claims 1 to 3, wherein the aluminum alloy material contains 0.05 to 0.6% Mg and 0.2 to 1.0% Mg. % Zn, further contains 0.1-1.5% Mn, 0.3
~1.2% Si, 0.3-1.5% Fe, 0.05
~0.20% Cu and 0.05-0.15% Zr
One or more selected from the group consisting of Al and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14723990A JP2936518B2 (en) | 1990-06-07 | 1990-06-07 | Aluminum alloy material with excellent corrosion resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14723990A JP2936518B2 (en) | 1990-06-07 | 1990-06-07 | Aluminum alloy material with excellent corrosion resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0441678A true JPH0441678A (en) | 1992-02-12 |
| JP2936518B2 JP2936518B2 (en) | 1999-08-23 |
Family
ID=15425726
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14723990A Expired - Lifetime JP2936518B2 (en) | 1990-06-07 | 1990-06-07 | Aluminum alloy material with excellent corrosion resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2936518B2 (en) |
-
1990
- 1990-06-07 JP JP14723990A patent/JP2936518B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JP2936518B2 (en) | 1999-08-23 |
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