JPH05132745A - Production of aluminum alloy excellent in formability - Google Patents
Production of aluminum alloy excellent in formabilityInfo
- Publication number
- JPH05132745A JPH05132745A JP32530691A JP32530691A JPH05132745A JP H05132745 A JPH05132745 A JP H05132745A JP 32530691 A JP32530691 A JP 32530691A JP 32530691 A JP32530691 A JP 32530691A JP H05132745 A JPH05132745 A JP H05132745A
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- treatment
- aluminum alloy
- formability
- room temperature
- subjected
- Prior art date
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は成形性に優れたアルミニ
ウム合金の製造方法に関するものであり、特に従来の２
０００系合金で代表されるＣｕ、Ｍｎ等を含有するアル
ミニウム合金において軟化処理後成形加工を施しても、
肌荒れを生じることのないアルミニウム合金の製造方法
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 having excellent formability, and particularly to the conventional method 2.
Even if an aluminum alloy containing Cu, Mn, etc. represented by a 000 series alloy is subjected to a forming process after the softening treatment,
The present invention relates to a method for producing an aluminum alloy that does not cause rough skin.
【０００２】[0002]
【従来の技術】従来成形用アルミニウム合金、例えば２
０２４等の合金は航空機用材料又はその他の構造用材料
として大量に使用されており、通常軟質材にて予備成形
加工を施し、次いで溶体化及び焼入れを行い、焼入れ直
後の強度の低い短時間の間に最終成形加工を行った後、
時効処理を施して高強度のアルミニウム合金とする製造
工程が実施されている。2. Description of the Related Art Conventional aluminum alloys for forming, eg 2
Alloys such as 024 are used in large quantities as materials for aircraft or other structural materials. Usually, soft materials are preformed, then solution heat treated and quenched to obtain a low strength short time immediately after quenching. After performing the final molding process in between,
A manufacturing process in which an aging treatment is performed to obtain a high-strength aluminum alloy is performed.
【０００３】[0003]
【発明が解決しようとする課題】従来の軟質材で１〜２
０％程度の予備成形加工を受けた部分は、その後の溶体
化、焼き入れ等の工程において著しく粗大な再結晶組織
となり、最終成形加工において表面に肌荒れ或いは微小
な割れが発生しアルミニウム製品としての性能を低下さ
せる原因となるものであった。The conventional soft material is 1-2.
The portion that has undergone preforming of about 0% has a remarkably coarse recrystallized structure in the subsequent steps such as solutionizing and quenching, and the surface is roughened or minute cracks occur in the final forming process, resulting in an aluminum product. It was a cause of lowering the performance.
【０００４】[0004]
【課題を解決するための手段】本発明はかかる状況に鑑
み鋭意検討の結果、板材、管材及び棒材などの軟質材に
施される圧延、抽伸、スウェージ、冷間鍛造などにおけ
る全ての冷間加工後に於いて再結晶粒が粗大とならず且
つ最終成形加工後も均一微細な結晶粒を有し、肌荒れの
生じない成形性に優れたアルミニウム合金の製造方法を
開発したものであり、請求項１記載の発明は、Ｃｕ４．
０〜７．０wt％、Ｍｎ０．１〜０．６wt％、Ｖ０．０１
〜０．２wt％、Ｚｒ０．０５〜０．３wt％、Ｔｉ０．０
１〜０．１５wt％を含有し、残部がＡｌと不可避不純物
とからなるアルミニウム合金鋳塊を均質化処理後、熱間
圧延及び冷間圧延を施し、次いで４７０〜５５０℃にて
溶体化処理後、室温以下の温度まで冷却した後、２０〜
７５％の加工を施した後、更に３６０〜５００℃にて軟
化処理を施し、その後の室温での導電率が４４〜４６％
ＩＡＣＳであることを特徴とする成形性に優れたアルミ
ニウム合金の製造方法であり、請求項２記載の発明は、
Ｃｕ４．０〜７．０wt％、Ｍｎ０．１〜０．６wt％、Ｖ
０．０１〜０．２wt％、Ｚｒ０．０５〜０．３wt％、Ｔ
ｉ０．０１〜０．１５wt％を含有し、残部がＡｌと不可
避不純物とからなるアルミニウム合金鋳塊を均質化処理
後、熱間圧延及び冷間圧延を施し、次いで４７０〜５５
０℃にて溶体化処理後、室温以下の温度まで冷却し、次
いで析出処理を行い、次いで２０〜７５％の加工を施し
た後、更に３６０〜５００℃にて軟化処理を施し、その
後の室温での導電率が４４〜４６％ＩＡＣＳであること
を特徴とする成形性に優れたアルミニウム合金の製造方
法である。DISCLOSURE OF THE INVENTION As a result of intensive investigations in view of such circumstances, the present invention has revealed that all cold workings such as rolling, drawing, swaging and cold forging applied to soft materials such as plate materials, pipe materials and bar materials. Claims: This is a method for producing an aluminum alloy which does not have coarse recrystallized grains after processing and has fine and uniform crystal grains even after final forming and has excellent formability without causing rough skin. The invention described in 1 is Cu4.
0-7.0 wt%, Mn 0.1-0.6 wt%, V0.01
~ 0.2 wt%, Zr0.05-0.3 wt%, Ti0.0
After homogenizing an aluminum alloy ingot containing 1 to 0.15 wt% and the balance of Al and unavoidable impurities, hot rolling and cold rolling are performed, and then solution treatment is performed at 470 to 550 ° C. , After cooling to a temperature below room temperature, 20 to
After processing 75%, softening treatment is further carried out at 360-500 ° C., and the conductivity at room temperature after that is 44-46%.
A method for producing an aluminum alloy having excellent formability, which is IACS, and the invention according to claim 2 is
Cu 4.0-7.0 wt%, Mn 0.1-0.6 wt%, V
0.01-0.2 wt%, Zr 0.05-0.3 wt%, T
The aluminum alloy ingot containing i of 0.01 to 0.15 wt% and the balance of Al and unavoidable impurities is homogenized, hot-rolled and cold-rolled, and then 470-55.
After solution treatment at 0 ° C., it is cooled to a temperature below room temperature, then precipitation treatment is performed, then 20 to 75% processing is performed, and then softening treatment is further performed at 360 to 500 ° C., then room temperature. The method for producing an aluminum alloy having excellent formability is characterized by having a conductivity of 44 to 46% IACS.
【０００５】[0005]
【作用】本発明において、合金組成を上記の如く限定し
たのは、次の理由によるものである。Ｃｕの含有量を
４．０〜７．０wt％と限定したのは、４．０wt％未満で
は成形加工後、溶体化処理及び時効処理を行っても十分
な強度が得られず、７．０wt％を超えるとＣｕ系金属間
化合物が析出し、靱性を低下するばかりか、冷間圧延性
及び成形加工性を低下させる為好ましくない。Ｍｎの含
有量を０．１〜０．６wt％、Ｚｒの含有量を０．０５〜
０．３wt％及びＴｉの含有量を０．０１〜０．１５wt％
と限定したのは、それぞれ下限未満では結晶粒が微細化
せず、成形加工性が改善されない為であり、また上限を
超えると冷間圧延性及び成形加工性を低下させる為好ま
しくない。Ｖの含有量を０．０１〜０．２wt％と限定し
たのは、０．０１wt％未満では耐熱性の効果が得られず
０．２wt％を超えると冷間圧延性及び成形加工性を低下
させる為好ましくない。In the present invention, the alloy composition is limited as described above for the following reason. The reason for limiting the Cu content to 4.0 to 7.0 wt% is that if it is less than 4.0 wt%, sufficient strength cannot be obtained even after solution treatment and aging treatment after molding, %, Cu-based intermetallic compound precipitates, which not only lowers the toughness but also lowers the cold rolling property and the formability, which is not preferable. Mn content is 0.1-0.6 wt%, Zr content is 0.05-
0.3 wt% and Ti content 0.01-0.15 wt%
The above limits are not preferable because the crystal grains do not become finer and the formability is not improved when the content is less than the lower limit, and the cold rolling property and the formability are deteriorated when the content exceeds the upper limit. The content of V is limited to 0.01 to 0.2 wt% because if it is less than 0.01 wt%, the effect of heat resistance cannot be obtained, and if it exceeds 0.2 wt%, cold rolling property and formability are deteriorated. It is not preferable because it causes
【０００６】次に製造方法を上記の如く限定したのは、
以下の理由によるものである。先ず均質化処理、熱間圧
延、冷間圧延した後、４７０〜５５０℃にて溶体化処理
後、室温以下の温度まで冷却するのは、溶質元素をマト
リックスに固溶させるか、又はその後Ｇ．Ｐ相もしくは
θ′中間相が析出した状態にする為である。４７０℃未
満では十分に固溶することができず、又５５０℃を超え
ると共晶溶融が起こり好ましくない。なおこの時の保持
時間は数分程度で良いが、できれば十分な時間の保持が
望ましい。又冷却速度は０．６℃／min.以上が良く、で
きれば水焼き入れが望ましい。次に析出処理を施すの
は、前述のＧ．Ｐ相又はθ′中間相の析出を適度に促進
し、再結晶粒の粗大化を阻害する為である。処理温度と
しては、１２０〜２００℃が好ましく、これは１２０℃
未満では析出が促進されず、２００℃を超えると析出相
の相変態が起こり好ましくない為である。またこの時の
保持時間は４０時間以下が望ましい。なお自然時効によ
っても時間を要するが析出は起こるので、長時間室温に
て放置する場合にはこの析出処理を行わなくてもよい。
次に２０〜７５％の加工を施すのは、微細再結晶粒を得
る為に必要な適度の量の転位を導入させる為である。２
０％未満では転位の量が少なく、又７５％を超えると転
位の量が多くなり何れも再結晶粒が大きくなるので好ま
しくない。次に３６０〜５００℃にて軟化処理を施すの
は、加工で導入された転位を微細均一なセル組織として
分布させ、それを核として微細な再結晶組織を得る為で
ある。３６０℃未満では十分に軟化されず、又５００℃
を超えると結晶粒が著しく成長する為好ましくない。な
おこの時の加熱速度は４０℃／hr以上が望ましい。又保
持時間は、高温側では数分〜数時間でよく低温側でも６
時間程度迄の保持時間で十分である。更に軟化後の冷却
は徐冷が望ましい。次に軟化後の室温での導電率を４４
〜４６％ＩＡＣＳと限定したのは、４４％ＩＡＣＳ未満
ではマトリックス中に溶質元素が固溶し過ぎ、又４６％
ＩＡＣＳを超えると析出物の量が多い状態にあり何れも
最終成形後の肌荒れ防止に効果が現れない為である。Next, the manufacturing method is limited as described above.
The reason is as follows. First, homogenization treatment, hot rolling, cold rolling, and then solution treatment at 470 to 550 ° C. and cooling to room temperature or lower are performed by dissolving the solute element in the matrix, or by G. This is because the P phase or the θ ′ intermediate phase is deposited. If it is less than 470 ° C, it cannot be sufficiently dissolved, and if it exceeds 550 ° C, eutectic melting occurs, which is not preferable. The holding time at this time may be several minutes, but if possible, it is desirable to hold it for a sufficient time. The cooling rate is preferably 0.6 ° C./min. Or higher, and water quenching is desirable if possible. Next, the precipitation treatment is performed according to G. This is because the precipitation of the P phase or the θ ′ intermediate phase is appropriately promoted and the coarsening of recrystallized grains is hindered. The treatment temperature is preferably 120 to 200 ° C, which is 120 ° C.
If it is less than 200 ° C., precipitation is not promoted, and if it exceeds 200 ° C., phase transformation of the precipitation phase occurs, which is not preferable. The holding time at this time is preferably 40 hours or less. Precipitation occurs although it takes time due to natural aging, so that the precipitation treatment does not have to be performed when it is left at room temperature for a long time.
Next, the processing of 20 to 75% is carried out in order to introduce a proper amount of dislocations necessary for obtaining fine recrystallized grains. Two
If it is less than 0%, the amount of dislocations is small, and if it exceeds 75%, the amount of dislocations is large and the recrystallized grains are large, which is not preferable. Next, the softening treatment is performed at 360 to 500 ° C. in order to distribute the dislocations introduced in the processing as a fine and uniform cell structure and obtain a fine recrystallized structure using the dislocations as nuclei. If it is less than 360 ° C, it is not softened sufficiently, and it is 500 ° C.
If it exceeds, crystal grains grow remarkably, which is not preferable. The heating rate at this time is preferably 40 ° C./hr or more. The holding time is several minutes to several hours on the high temperature side and 6 on the low temperature side.
A holding time up to about an hour is sufficient. Further, the cooling after softening is preferably slow cooling. Next, the softness at room temperature after softening is 44
The limit of ~ 46% IACS is that the solute element is too solid-solubilized in the matrix below 44% IACS, and is 46%.
This is because if the IACS is exceeded, the amount of precipitates will be large and none of the effects will be effective in preventing rough skin after final molding.
【０００７】[0007]
【実施例】表１に示す組成の合金を通常の溶製法により
鋳造し、面削後、熱間圧延、冷間圧延を経て、厚さ２mm
の板材とした。この板材を表２に示す本発明法、比較法
による処理条件及び従来の焼鈍処理によりそれぞれ処理
を行って試料を得た。なお何れの場合も溶体化処理後は
室温迄水冷し、軟化処理は８０℃／hr. にて加熱後、２
５０℃迄２５℃／hr. の冷却速度で徐冷した。この軟化
後の室温にて導電率を測定した。この様にして得た本発
明材、比較材及び従来材についてその性能を試みる為
に、表３に示す０〜２０％の予備成形加工（Ｌ及びＬＴ
方向引張）を行い、次に溶体化焼入れ処理（５００℃×
１hr. 水冷）を実施後直ちに最終成形加工（２〜１０％
Ｌ及びＬＴ方向引張）を行って肌荒れの有無を確認し
た。EXAMPLE An alloy having the composition shown in Table 1 was cast by an ordinary melting method, face-cut, hot-rolled and cold-rolled to a thickness of 2 mm.
It was used as a plate material. Samples were obtained by subjecting this plate material to the treatment conditions according to the method of the present invention and the comparative method shown in Table 2 and the conventional annealing treatment. In either case, after solution treatment, water-cooling to room temperature, softening treatment at 80 ° C / hr.
It was gradually cooled to 50 ° C. at a cooling rate of 25 ° C./hr. The electrical conductivity was measured at room temperature after this softening. In order to test the performances of the inventive material, the comparative material and the conventional material thus obtained, 0 to 20% of the preforming process (L and LT) shown in Table 3 was performed.
Direction tensile), and then solution heat treatment (500 ℃ x
Immediately after carrying out 1 hr. Water cooling, final molding process (2-10%)
The presence or absence of rough skin was confirmed by performing (L and LT direction tension).
【０００８】[0008]
【表１】 [Table 1]
【０００９】[0009]
【表２】 [Table 2]
【００１０】[0010]
【表３】 [Table 3]
【００１１】表３から明らかなように本発明材試料No．
１〜８はいずれも軟化処理後の最大結晶粒が微細であ
り、種々の加工率で予備成形加工を行っても、最終成形
加工後の肌荒れは発生しなかった。これに対し本発明製
造方法の範囲をはずれる比較材試料No．９〜１２は肌荒
れまたは割れを発生した。As is apparent from Table 3, the material sample No.
In all of Nos. 1 to 8, the maximum crystal grains after the softening treatment were fine, and even when preforming was performed at various processing rates, the roughening after the final forming did not occur. On the other hand, the comparative material sample No. out of the range of the manufacturing method of the present invention. 9-12 generated rough skin or cracks.
【００１２】[0012]
【発明の効果】このように本発明製造方法によれば、軟
化処理材で予備成形加工をうけた部分は、後工程で溶体
化焼入れ処理を行っても均一微細な再結晶組織を有し、
最終成形加工後も肌荒れを発生しない成形性に優れたア
ルミニウム合金の製造が可能であり、工業上顕著な効果
を奏するものである。As described above, according to the manufacturing method of the present invention, the portion which has been preformed with the softening-treated material has a uniform fine recrystallized structure even if the solution hardening treatment is performed in the subsequent step,
It is possible to produce an aluminum alloy having excellent formability that does not cause surface roughness even after the final forming process, and it is possible to achieve a remarkable industrial effect.
Claims (2)
０．６wt％、Ｖ０．０１〜０．２wt％、Ｚｒ０．０５〜
０．３wt％、Ｔｉ０．０１〜０．１５wt％を含有し、残
部がＡｌと不可避不純物とからなるアルミニウム合金鋳
塊を均質化処理後、熱間圧延及び冷間圧延を施し、次い
で４７０〜５５０℃にて溶体化処理後、室温以下の温度
まで冷却した後、２０〜７５％の加工を施した後、更に
３６０〜５００℃にて軟化処理を施し、その後の室温で
の導電率が４４〜４６％ＩＡＣＳであることを特徴とす
る成形性に優れたアルミニウム合金の製造方法。1. Cu 4.0-7.0 wt%, Mn 0.1
0.6 wt%, V0.01-0.2 wt%, Zr0.05-
After homogenizing an aluminum alloy ingot containing 0.3 wt% and 0.01 to 0.15 wt% of Ti and the balance of Al and unavoidable impurities, hot rolling and cold rolling are performed, and then 470 to 550. After solution treatment at ℃, after cooling to a temperature below room temperature, after processing 20 to 75%, further softening at 360 to 500 ℃, the subsequent conductivity at room temperature is 44 ~ A method for producing an aluminum alloy having excellent formability, which is 46% IACS.
０．６wt％、Ｖ０．０１〜０．２wt％、Ｚｒ０．０５〜
０．３wt％、Ｔｉ０．０１〜０．１５wt％を含有し、残
部がＡｌと不可避不純物とからなるアルミニウム合金鋳
塊を均質化処理後、熱間圧延及び冷間圧延を施し、次い
で４７０〜５５０℃にて溶体化処理後、室温以下の温度
まで冷却し、次いで析出処理を行い、次いで２０〜７５
％の加工を施した後、更に３６０〜５００℃にて軟化処
理を施し、その後の室温での導電率が４４〜４６％ＩＡ
ＣＳであることを特徴とする成形性に優れたアルミニウ
ム合金の製造方法。2. Cu 4.0-7.0 wt%, Mn 0.1
0.6 wt%, V0.01-0.2 wt%, Zr0.05-
After homogenizing an aluminum alloy ingot containing 0.3 wt% and 0.01 to 0.15 wt% of Ti and the balance of Al and unavoidable impurities, hot rolling and cold rolling are performed, and then 470 to 550. After solution treatment at ℃, cooled to a temperature below room temperature, followed by precipitation treatment, then 20-75
%, And then a softening treatment at 360 to 500 ° C., and the conductivity at room temperature thereafter is 44 to 46% IA.
A method for producing an aluminum alloy having excellent formability, which is CS.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32530691A JPH05132745A (en) | 1991-11-12 | 1991-11-12 | Production of aluminum alloy excellent in formability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32530691A JPH05132745A (en) | 1991-11-12 | 1991-11-12 | Production of aluminum alloy excellent in formability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05132745A true JPH05132745A (en) | 1993-05-28 |
Family
ID=18175350
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32530691A Pending JPH05132745A (en) | 1991-11-12 | 1991-11-12 | Production of aluminum alloy excellent in formability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05132745A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008072972A1 (en) * | 2006-12-13 | 2008-06-19 | Hydro Aluminium As | Aluminium casting alloy, method for the manufacture of a casting and cast component for combustion engines |
| WO2012044450A3 (en) * | 2010-09-08 | 2012-07-05 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
| EP2625302A4 (en) * | 2010-10-08 | 2015-10-07 | Alcoa Inc | Improved 2xxx aluminum alloys, and methods for producing the same |
| US9587298B2 (en) | 2013-02-19 | 2017-03-07 | Arconic Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
| US9926620B2 (en) | 2012-03-07 | 2018-03-27 | Arconic Inc. | 2xxx aluminum alloys, and methods for producing the same |
| CN110284086A (en) * | 2019-07-29 | 2019-09-27 | 中国船舶重工集团公司第十二研究所 | A method of it eliminates and crystallizes phase segregation in casting Al-Cu manganese alloy |
-
1991
- 1991-11-12 JP JP32530691A patent/JPH05132745A/en active Pending
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008072972A1 (en) * | 2006-12-13 | 2008-06-19 | Hydro Aluminium As | Aluminium casting alloy, method for the manufacture of a casting and cast component for combustion engines |
| EP2097551A1 (en) * | 2006-12-13 | 2009-09-09 | Hydro Aluminium As | Aluminium casting alloy, method for the manufacture of a casting and cast component for combustion engines |
| EP2097551A4 (en) * | 2006-12-13 | 2010-09-22 | Hydro Aluminium As | Aluminium casting alloy, method for the manufacture of a casting and cast component for combustion engines |
| US9194028B2 (en) | 2010-09-08 | 2015-11-24 | Alcoa Inc. | 2xxx aluminum alloys, and methods for producing the same |
| US8999079B2 (en) | 2010-09-08 | 2015-04-07 | Alcoa, Inc. | 6xxx aluminum alloys, and methods for producing the same |
| WO2012044450A3 (en) * | 2010-09-08 | 2012-07-05 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
| US9249484B2 (en) | 2010-09-08 | 2016-02-02 | Alcoa Inc. | 7XXX aluminum alloys, and methods for producing the same |
| US9359660B2 (en) | 2010-09-08 | 2016-06-07 | Alcoa Inc. | 6XXX aluminum alloys, and methods for producing the same |
| EP2625302A4 (en) * | 2010-10-08 | 2015-10-07 | Alcoa Inc | Improved 2xxx aluminum alloys, and methods for producing the same |
| US9926620B2 (en) | 2012-03-07 | 2018-03-27 | Arconic Inc. | 2xxx aluminum alloys, and methods for producing the same |
| US9587298B2 (en) | 2013-02-19 | 2017-03-07 | Arconic Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
| CN110284086A (en) * | 2019-07-29 | 2019-09-27 | 中国船舶重工集团公司第十二研究所 | A method of it eliminates and crystallizes phase segregation in casting Al-Cu manganese alloy |
| CN110284086B (en) * | 2019-07-29 | 2020-12-01 | 中国船舶重工集团公司第十二研究所 | Method for eliminating segregation of crystalline phase in cast aluminum-copper-manganese alloy |
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