JPH03193841A - Aluminum alloy for cold forming having excellent work hardenability - Google Patents
Aluminum alloy for cold forming having excellent work hardenabilityInfo
- Publication number
- JPH03193841A JPH03193841A JP33325689A JP33325689A JPH03193841A JP H03193841 A JPH03193841 A JP H03193841A JP 33325689 A JP33325689 A JP 33325689A JP 33325689 A JP33325689 A JP 33325689A JP H03193841 A JPH03193841 A JP H03193841A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- cold forming
- alloy
- cold
- dislocations
- 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.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 38
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 238000005482 strain hardening Methods 0.000 claims description 9
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- 238000011282 treatment Methods 0.000 abstract description 11
- 229910052802 copper Inorganic materials 0.000 abstract description 7
- 238000005098 hot rolling Methods 0.000 abstract description 4
- 238000005266 casting Methods 0.000 abstract description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 238000005097 cold rolling Methods 0.000 abstract description 3
- 238000002844 melting Methods 0.000 abstract description 3
- 230000008018 melting Effects 0.000 abstract description 3
- 238000007670 refining Methods 0.000 abstract description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 2
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 229910052725 zinc Inorganic materials 0.000 abstract 1
- 229910052726 zirconium Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 9
- 210000004027 cell Anatomy 0.000 description 5
- 238000001000 micrograph Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000003917 TEM image Methods 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000010960 cold rolled steel Substances 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 230000032683 aging Effects 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910018134 Al-Mg Inorganic materials 0.000 description 1
- 229910018467 Al—Mg Inorganic materials 0.000 description 1
- CDBYLPFSWZWCQE-UHFFFAOYSA-L Sodium Carbonate Chemical compound [Na+].[Na+].[O-]C([O-])=O CDBYLPFSWZWCQE-UHFFFAOYSA-L 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 210000003850 cellular structure Anatomy 0.000 description 1
- 239000003984 copper intrauterine device Substances 0.000 description 1
- 210000003127 knee Anatomy 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000004570 mortar (masonry) Substances 0.000 description 1
- 238000007591 painting process Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Landscapes
- Body Structure For Vehicles (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野コ
本発明は加工硬化能が優れた冷間成形加工用アルミニウ
ム合金に関し、さらに詳しくは、主に自動車ボディ用ア
ルミニウム合金として、強度および延性のバランスが良
好な加工硬化能が優れた冷間成形加工用アルミニウム合
金に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to an aluminum alloy for cold forming with excellent work hardenability. The present invention relates to an aluminum alloy for cold forming which has good work hardenability.
［従来技術］
従来より、自動車ボディ用アルミニウム合金としては、
例えば、特公昭５６−０３１８５８号公報および特公昭
５６−０３１８６０号公報により提案されている。[Prior art] Traditionally, aluminum alloys for automobile bodies include:
For example, it has been proposed in Japanese Patent Publication No. 56-031858 and Japanese Patent Publication No. 56-031860.
そして、特公昭５６−０３１８５８号号公報に提案され
ているアルミニウム合金は、Ｍｇ １５〜５．５ｗｔ％
、Ｚｎ ＯＪ 〜１．２ｗｔ％、Ｃｕ ０．３〜１．２
ｗｔ％を含有し、残部Ａｌおよび不可避不純物からなる
ものである。The aluminum alloy proposed in Japanese Patent Publication No. 56-031858 contains 15 to 5.5 wt% Mg.
, Zn OJ ~1.2wt%, Cu 0.3~1.2
wt%, and the remainder consists of Al and unavoidable impurities.
また、特公昭５６−０３１８６０号公報に提案されてい
るアルミニウム合金は、Ｍｇ ３４〜５．５ｗｔ％、Ｚ
ｎ ０．５〜２．Ｏｗｔ％、Ｃｕ ０．：３−１．２ｗ
ｔ％を必須成分として含有し、さらに、Ｍｎ ０．０５
〜０．４ｖｔ％、Ｏｒ ０．０５〜０．２５ｗｔ％、Ｚ
ｒ ０．０５〜０．２５ｗｔ％、ＶＯ１Ｏ１〜０．１５
ｗｔ％の内から選んだ１種または２種以上を含有し、残
部Ａｌおよび不可避不純物からなるものである。Furthermore, the aluminum alloy proposed in Japanese Patent Publication No. 56-031860 contains 34 to 5.5 wt% Mg, Z
n 0.5-2. Owt%, Cu 0. :3-1.2w
t% as an essential component, and further contains Mn 0.05
~0.4vt%, Or 0.05~0.25wt%, Z
r 0.05-0.25wt%, VO1O1-0.15
% by weight, and the remainder consists of Al and unavoidable impurities.
しかしながら、上記に説明したアルミニウム合金は、強
度−延性バランスに優れた性質を有するものの、冷間圧
延鋼板と比較すると成形性が劣っているという問題があ
る。そして、成形性は引張試験における伸び率と強い相
関関係があることは良く知られている。However, although the aluminum alloy described above has properties with an excellent balance of strength and ductility, it has a problem in that its formability is inferior compared to cold rolled steel sheets. It is well known that formability has a strong correlation with the elongation rate in a tensile test.
上記に説明した従来技術としての各公報に提案されてい
るアルミニウム合金は、伸び率は３０％程度であり、冷
間圧延鋼板の伸び率３６〜５０％と比較しても可なり劣
っており、このことが成形性において劣っている原因と
なっている。The elongation rate of the aluminum alloys proposed in each publication as the prior art described above is about 30%, which is considerably inferior to the elongation rate of cold rolled steel sheets, which is 36 to 50%. This is the cause of poor moldability.
従って、成形性の優れたアルミニウム合金が要望されて
いる。Therefore, an aluminum alloy with excellent formability is desired.
［発明が解決しようとする課題］
本発明は上記に説明した従来技術におけるアルミニウム
合金を自動車ボディに適用するためには、成形性をさら
に向上させることが必要であり、それには冷間圧延鋼板
に匹敵する伸び率を有するものとすることが必要である
ことに鑑み、本発明者は鋭意研究を行なった結果、アル
ミニウム合金の延性の機構について、ＡｌにＭｇとＣｕ
を同時に含有させることによって、アルミニウム合金の
加工硬化能が大幅に増大し、冷間圧延鋼板に匹敵する伸
び率を示すことを知見し、本発明に係る加工硬化能が優
れた冷間成形加工用アルミニウム合金を開発したのであ
る。[Problems to be Solved by the Invention] In order to apply the aluminum alloy in the prior art described above to automobile bodies, it is necessary to further improve the formability. Considering that it is necessary to have comparable elongation rates, the present inventor conducted extensive research and found that the ductility mechanism of aluminum alloys is
It has been found that by simultaneously containing aluminum alloys, the work hardening ability of the aluminum alloy is greatly increased and the elongation rate is comparable to that of cold rolled steel sheets. He developed an aluminum alloy.
［問題点を解決するための手段］
本発明に係る加工硬化能が優れた冷開成形加工用アルミ
ニウム合金は、
（１） Ｍｇ＋ Ｃｕ ７〜１０ｗｔ％を含有し、残部
Ａｌおよび不可避不純物からなり、冷間成形加工後、セ
ル組織を含まず、転位が直線状に配列された組織を有す
ることを特徴とする加工硬化能が優れた冷開成形加工用
アルミニウム合金を第１の発明とし、
（２） Ｍｇ＋ｃｕ ７〜１０ｗｔ％
を含有し、さらに、
Ｚｎ ０．５〜１．５ｗｔ％、Ｍｎ ０．０５〜０．５
ｗｔ％、Ｃｒ ０．０５〜ＯＪｗｔ％、Ｚ ｒ ０．０
５〜０．３ｖｔ％の内から選んだ１種または２種以上
を含有し、残部Ａｌおよび不可避不純物からなり、冷間
成形加工後、セル組織を含まず、転位が直線状に配列さ
れた組織を有することを特徴とする加工硬化能が優れた
冷間成形加工用アルミニウム合金を第２の発明とする２
つの発明よりなるものである。[Means for Solving the Problems] The aluminum alloy for cold-open forming with excellent work hardenability according to the present invention contains (1) 7 to 10 wt% of Mg+Cu, and the remainder consists of Al and unavoidable impurities; The first invention is an aluminum alloy for cold-open forming which has excellent work hardening ability and which does not contain a cell structure and has a structure in which dislocations are linearly arranged after cold forming. ) Contains Mg+cu 7 to 10 wt%, and further contains Zn 0.5 to 1.5 wt%, Mn 0.05 to 0.5
wt%, Cr 0.05~OJwt%, Z r 0.0
A structure containing one or more selected from 5 to 0.3 vt%, the remainder consisting of Al and unavoidable impurities, and after cold forming processing, does not contain a cell structure and has dislocations arranged in a straight line. A second invention provides an aluminum alloy for cold forming which has excellent work hardening ability.
This invention consists of three inventions.
本発明に係る加工硬化能が優れた冷開成形加工用アルミ
ニウム合金について、以下詳細に説明する。The aluminum alloy for cold-open forming with excellent work hardenability according to the present invention will be described in detail below.
一般的に、Ｍｇを４，５ｗｔ％程度含有するアルミニウ
ム合金は、積層欠陥エネルギーが大きく低下しないため
、例えば、自動車ボディの冷開成形加工を行なうと第１
図（ａ）の顕微鏡写真に示すようにセル組織になるので
、冷間成形加工における鋼板並の延性向上を期待するこ
とはできない。In general, aluminum alloys containing about 4.5 wt% Mg do not have a significant drop in stacking fault energy, so for example, when cold-forming an automobile body, the first
As shown in the micrograph in Figure (a), it becomes a cellular structure, so it cannot be expected to improve the ductility as much as a steel plate in cold forming.
しかし、積層欠陥エネルギーが低下すると、加工を行な
った時の転位の交差滑りが困難となるため、転位が一つ
の滑り面のみを滑るようになって、セル組織を形成し難
くなり、転位が直線状に流れる組織となって、加工硬化
能が増大することになる。However, when the stacking fault energy decreases, it becomes difficult for dislocations to cross-slide during processing, so dislocations slide only on one sliding surface, making it difficult to form a cell structure, and dislocations become linear. This results in an increased work hardening ability, resulting in a flowing structure.
なお、本発明に係る加工硬化能が優れた冷間成形加工用
アルミニウム合金における合金組織は、即ち、冷間成形
加工後、セル組織を含まず、転位が直線状に配列された
組織であり、例えば、自動車ボディ等の最終用途におけ
る製品および部品へのプレス等の冷間成形加工を行なう
際に発現するものであり、通常のアルミニウム合金の鍛
造−熱間加工あるいはこれに伴う冷間側ニー熱処理の段
階においては発現しない。これは、熱的に活性化された
転位が、回復もしくは再結晶によって消滅するためであ
る。The alloy structure of the cold-forming aluminum alloy with excellent work hardenability according to the present invention is a structure in which dislocations are linearly arranged without containing a cell structure after cold-forming. For example, it occurs when performing cold forming processing such as pressing on products and parts for end use such as automobile bodies, and is caused by ordinary forging-hot processing of aluminum alloys or the accompanying cold side knee heat treatment. It does not appear at this stage. This is because thermally activated dislocations disappear through recovery or recrystallization.
本発明に係る加工硬化能が優れた冷間成形加工用アルミ
ニウム合金の含有成分および成分割合について説明する
。The components and component ratios of the cold-forming aluminum alloy with excellent work hardenability according to the present invention will be explained.
Ｍｇは積層欠陥エネルギーを低くし、加工硬化能を増大
させることにより、強度および伸び率を高くする元素で
あり、また、Ｃｕは積層欠陥エネルギーを低くし、加工
硬化能を増大させることによって、強度および伸び率を
高くする元素であり、また、Ｃｕはプレス成形後の焼付
塗装処理において時効硬化させる効果を育しており、さ
らに、ＣｕはＡｌ−Ｍｇ系合金において問題となる応力
腐蝕割れを防止する効果を育し、Ｍｇ十Ｃｕの含有量が
７ｗｔ％未満では上記に説明したＭｇとＣｕの効果が充
分に発揮されず、また、ＩＫｔ％を越えて含有させると
熱間加工性および冷間加工性が悪化する。Mg is an element that increases strength and elongation by lowering stacking fault energy and increasing work hardening ability, and Cu is an element that increases strength by lowering stacking fault energy and increasing work hardening ability. Cu is an element that increases the elongation rate, and also has an age-hardening effect in the baking painting process after press forming.Cu also prevents stress corrosion cracking, which is a problem in Al-Mg alloys. If the content of Mg and Cu is less than 7wt%, the effects of Mg and Cu explained above will not be fully exhibited, and if the content exceeds IKt%, hot workability and cold workability will be affected. Workability deteriorates.
よって、Ｍｇ十Ｃｕ含育量は ７〜１０ｗｔ％とする。Therefore, the Mg and Cu content is set to 7 to 10 wt%.
Ｚｎは応力腐蝕割れを防止する効果と、焼入れ後の室温
時効により強度を増加させる効果を有する元素であり、
含有量が０．５ｗｔ％未満ではこのような効果は充分で
はなく、また、１．５ｗｔ％を越えて含有させると伸び
率が低下し、成形性が悪化する。よって、Ｚｎ含有量は
０．５〜１ 、５ｗｔ％とする。Zn is an element that has the effect of preventing stress corrosion cracking and increasing strength through room temperature aging after quenching.
If the content is less than 0.5 wt%, such effects are not sufficient, and if the content exceeds 1.5 wt%, the elongation rate decreases and moldability deteriorates. Therefore, the Zn content is set to 0.5 to 1.5 wt%.
Ｍｎ、Ｏｒは応力腐蝕割れを防止する効果と、結晶粒を
微細化し、成形性を向上させる効果を有する元素であり
、Ｍｎ含有量が０．０５ｗｔ％未満、Ｃｒ含有量がｏ、
ｏｓｗｔ％未満では上記の効果は不充分であり、また、
Ｍｎ含有量が０．５ｗｔ％、Ｃｒ含有量が０．３ｗｔ％
をそれぞれ越えると粗大な金属間化合物が晶出し易くな
り、成形性が悪化する。よって、Ｍｎ含有量は０．０５
〜０．５ｗｔ％、Ｃｒ含有量は０．０５〜ＯＪｗｔ％と
する。Mn and Or are elements that have the effect of preventing stress corrosion cracking, refining crystal grains, and improving formability, and the Mn content is less than 0.05 wt%, the Cr content is o,
If it is less than oswt%, the above effect is insufficient, and
Mn content is 0.5wt%, Cr content is 0.3wt%
If these values are exceeded, coarse intermetallic compounds tend to crystallize, resulting in poor formability. Therefore, the Mn content is 0.05
~0.5wt%, and the Cr content is 0.05~OJwt%.
Ｚｒは結晶粒を微細化し、成形性を向上させる元素であ
り、含有量が０．０５ｗｔ％未満ではこのような効果は
不充分であり、また、０．３ｖｔ％を越えて含有させる
と粗大な金属間化合物が晶出し易くなり、成形性が悪く
なる。よって、Ｚｒ含有量は０．０５〜０．３ｗｔ％と
する。Zr is an element that refines crystal grains and improves formability.If the content is less than 0.05wt%, this effect is insufficient, and if the content exceeds 0.3wt%, it will cause coarse grains. Intermetallic compounds tend to crystallize, resulting in poor formability. Therefore, the Zr content is set to 0.05 to 0.3 wt%.
本発明に係る加工硬化能が優れた冷開成形加工用アルミ
ニウム合金は、通常の溶解、鋳造、均質化処理、熱間圧
延、冷間圧延を行なった後、Ｔ４処理の最終調質処理を
行なうことにより製造される。なお、溶体化処理の最適
温度条件は、Ｍｇ含有量およびＣｕ含有量が変化すると
、それにつれて変化するが、ＭｇとＣｕを充分に固溶さ
せるためには、４５０〜５００℃の範囲とするのがよい
。The aluminum alloy for cold-open forming with excellent work hardening ability according to the present invention is subjected to the usual melting, casting, homogenizing treatment, hot rolling, and cold rolling, and then to the final tempering treatment of T4 treatment. Manufactured by The optimum temperature conditions for solution treatment will change as the Mg content and Cu content change, but in order to sufficiently dissolve Mg and Cu, it should be in the range of 450 to 500°C. Good.
また、４５０〜５００℃の温度において１時間の溶体化
処理を行なった後、水焼入れを行なう通常の処理を行な
う以外にも、連続焼鈍炉を使用して短時間急速加熱後、
空冷処理を行なうことによっても、高い強度および伸び
率を得る゛ことができる。In addition to the usual treatment of solution treatment at a temperature of 450 to 500°C for one hour followed by water quenching, we can also perform rapid heating for a short time using a continuous annealing furnace.
High strength and elongation can also be obtained by performing air cooling treatment.
第１図（ａ）にＭｇ含有量４．５ｗｔ％の、従来技術に
よる合金の５％ストレッチ材の顕微鏡写Ｘ（Ｔ ＥＭ像
、室温３０，０００倍）を示すが、セル組織が顕著に形
成されていることが認められ、第１図（ｂ）は本発明に
係る加工硬化能が優れた冷間成形加工用アルミニウム合
金、即ち、Ｍｇ含有量８ｗｔ％の５％ストレッチ材の顕
微鏡写真（ＴＥＭ像、室温７５．０００倍）を示してあ
り、転位が直線状に流れていることが認められる。Figure 1(a) shows a micrograph X (TEM image, 30,000x room temperature) of a 5% stretch material made of a conventional alloy with an Mg content of 4.5 wt%, and a cell structure is clearly formed. Figure 1(b) is a micrograph (TEM (75,000 times room temperature), and it is observed that dislocations flow in a straight line.
［実 施 例コ
本発明に係る加工硬化能が優れた冷間成形加工用アルミ
ニウム合金の実施例を比較例と共に説明する。[Example] Examples of the aluminum alloy for cold forming with excellent work hardenability according to the present invention will be described together with comparative examples.
実施例
第１表（こ示す含有成分および成分割合のアルミニウム
合金を溶解、鋳造して鋳塊を製造した。Examples Table 1 (An ingot was produced by melting and casting an aluminum alloy having the components and proportions shown in the table.
４８０℃×２４時間の均質化処理を行なった後、熱間圧
延により５ｍｍの厚さとし、４００Ｘ１時間の中間焼鈍
を行ない、ソーダ洗浄を行なった後、冷間圧延により２
ｍｍの厚さとなし、４００℃×１時間の中間焼鈍を経て
、再び冷間圧延を行なってＩｎｏｎ厚さのアルミニウム
合金板を製作した。After homogenizing at 480°C for 24 hours, it was hot rolled to a thickness of 5mm, intermediately annealed at 400°C for 1 hour, washed with soda, and then cold rolled to a thickness of 5mm.
After intermediate annealing at 400° C. for 1 hour, cold rolling was performed again to produce an aluminum alloy plate with Inon thickness.
最終調質を
■ ４８０℃×１時間保持−水冷
■ ４８０℃×３０秒間保持−強制空冷の２つの条件で
溶体化処理を行なった後、１週間以上室温に放置し、自
然時効させるＴ４処理を行なった。After the final thermal refining is carried out under two conditions: (1) holding at 480°C for 1 hour - water cooling and (2) holding at 480°C for 30 seconds - forced air cooling, T4 treatment is carried out by leaving it at room temperature for over a week and allowing natural aging. I did it.
このようにして製作されたＴ４材に対して、弓張試験を
実施し、機械的特性を調査した。The T4 material produced in this way was subjected to a bow tension test to investigate its mechanical properties.
第２表にその結果を示す。Table 2 shows the results.
第
１
表
Ｎ０１５
ＮＯ１６は比較例
Ｎｏ、５．Ｎｏ、６は比較例、Ｎｏ、８は熱間圧延割れ
で測定不能この第２表から明らかなように、本発明に係
る加工硬化能が優れた冷間成形加工用アルミニウム合金
は、伸びが３３〜３８％であり、比較例のアルミニウム
合金の伸び３０％程度を大きく上回っていることがわか
る。Table 1 No. 15 No. 16 is Comparative Example No. 5. No. 6 is a comparative example, and No. 8 is a hot rolling crack that cannot be measured. It can be seen that the elongation is ~38%, which greatly exceeds the elongation of the aluminum alloy of the comparative example, which is about 30%.
また、Ｍｇ＋Ｃｕ含有量が７ｗｔ％を下回ると、充分な
特性を発揮できず、１０ｗｔ％を越えると熱間圧延にお
いて割れが発生して加工を行なうことが不可能であった
。Further, when the Mg+Cu content was less than 7 wt%, sufficient properties could not be exhibited, and when it exceeded 10 wt%, cracks occurred during hot rolling, making it impossible to process.
［発明の効果〕
以上説明したように、本発明に係る加工硬化能が優れた
冷間成形加工用アルミニウム合金は上記の構成であるか
ら、主として自動車ボディ用アルミニウム合金として強
度−延性バランスに優れた特性を有するという効果があ
る。[Effects of the Invention] As explained above, since the aluminum alloy for cold forming with excellent work hardening ability according to the present invention has the above structure, it can be used mainly as an aluminum alloy for automobile bodies with an excellent strength-ductility balance. It has the effect of having characteristics.
第１図（ａ）は従来のアルミニウム合金の５％ストレッ
チ材の顕微鏡写真（ＴＥＭ像、室温３０．０００倍）、
第１図（ｂ）は本発明に係る加工硬化能が優れた冷間成
形加工用アルミニウム合金の５％ストレッチ材の顕微鏡
写真（ＴＥＭ像、室温７５，０００倍）である。
５、補正命令の日付
平成０２年０３月２７日 （発送臼）
６、補正の対象
（１）明細書の図面の簡単な説明の欄
（２）第１図（ａＸｂ）
７、補正の内容
別紙の通りFigure 1 (a) is a micrograph (TEM image, room temperature, 30.000x) of a 5% stretch material made of conventional aluminum alloy.
FIG. 1(b) is a micrograph (TEM image, 75,000 times room temperature) of a 5% stretch material of an aluminum alloy for cold forming with excellent work hardenability according to the present invention. 5. Date of amendment order: March 27, 2000 (Shipping mortar) 6. Subject of amendment (1) Brief explanation column of drawings in the specification (2) Figure 1 (aXb) 7. Attachment with details of amendment street
Claims (2)
成形加工後、セル組織を含まず、転位が直線状に配列さ
れた組織を有することを特徴とする加工硬化能が優れた
冷間成形加工用アルミニウム合金。(1) Contains 7 to 10 wt% of Mg + Cu, the balance is Al and unavoidable impurities, and after cold forming, it does not contain a cell structure and has a structure in which dislocations are linearly arranged. An aluminum alloy with excellent cold forming properties.
％、Ｃｒ０．０５〜０．３ｗｔ％、Ｚｒ０．０５〜０．
３ｗｔ％の内から選んだ１種または２種以上 を含有し、残部Ａｌおよび不可避不純物からなり、冷間
成形加工後、セル組織を含まず、転位が直線状に配列さ
れた組織を有することを特徴とする加工硬化能が優れた
冷間成形加工用アルミニウム合金。(2) Contains Mg+Cu7-10wt%, and further contains Zn0.5-1.5wt%, Mn0.05-0.5wt%
%, Cr0.05-0.3wt%, Zr0.05-0.
3wt% of one or more selected from the group consisting of Al and unavoidable impurities, and after cold forming, it does not contain a cell structure and has a structure in which dislocations are linearly arranged. An aluminum alloy for cold forming with excellent work hardening ability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33325689A JPH03193841A (en) | 1989-12-22 | 1989-12-22 | Aluminum alloy for cold forming having excellent work hardenability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33325689A JPH03193841A (en) | 1989-12-22 | 1989-12-22 | Aluminum alloy for cold forming having excellent work hardenability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03193841A true JPH03193841A (en) | 1991-08-23 |
Family
ID=18264075
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP33325689A Pending JPH03193841A (en) | 1989-12-22 | 1989-12-22 | Aluminum alloy for cold forming having excellent work hardenability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03193841A (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4851811A (en) * | 1971-10-29 | 1973-07-20 | ||
| JPS5631860A (en) * | 1979-08-23 | 1981-03-31 | Kawasaki Heavy Ind Ltd | Coupling connecting device for railway rolling stock |
| JPS5631858A (en) * | 1979-08-24 | 1981-03-31 | Shibaura Eng Works Ltd | Sound insulating operating chamber for railroad maintenance machine |
| JPH01225738A (en) * | 1988-03-03 | 1989-09-08 | Sky Alum Co Ltd | Heat treatment-type aluminum alloy rolled plate for forming and its manufacture |
-
1989
- 1989-12-22 JP JP33325689A patent/JPH03193841A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4851811A (en) * | 1971-10-29 | 1973-07-20 | ||
| JPS5631860A (en) * | 1979-08-23 | 1981-03-31 | Kawasaki Heavy Ind Ltd | Coupling connecting device for railway rolling stock |
| JPS5631858A (en) * | 1979-08-24 | 1981-03-31 | Shibaura Eng Works Ltd | Sound insulating operating chamber for railroad maintenance machine |
| JPH01225738A (en) * | 1988-03-03 | 1989-09-08 | Sky Alum Co Ltd | Heat treatment-type aluminum alloy rolled plate for forming and its manufacture |
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