JP2001020027A - Al-Mg-Si-Cu ALLOY SHEET EXCELLENT IN CORROSION RESISTANCE AND FORMABILITY, AND ITS MANUFACTURE - Google Patents
Al-Mg-Si-Cu ALLOY SHEET EXCELLENT IN CORROSION RESISTANCE AND FORMABILITY, AND ITS MANUFACTUREInfo
- Publication number
- JP2001020027A JP2001020027A JP2000034464A JP2000034464A JP2001020027A JP 2001020027 A JP2001020027 A JP 2001020027A JP 2000034464 A JP2000034464 A JP 2000034464A JP 2000034464 A JP2000034464 A JP 2000034464A JP 2001020027 A JP2001020027 A JP 2001020027A
- Authority
- JP
- Japan
- Prior art keywords
- formability
- solution treatment
- corrosion resistance
- producing
- alloy sheet
- 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.)
- Withdrawn
Links
Landscapes
- Metal Rolling (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車のボディシ
ートや部品、各種機械器具、家電部品等の素材として使
用する、成形加工用Ａｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板と
その製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an Al-Mg-Si-Cu alloy plate for forming and used as a material for body sheets and parts of automobiles, various machine tools, home electric parts and the like, and a method for producing the same.
【０００２】[0002]
【従来の技術】高成形性および高強度を要求する用途、
例えば自動車のボディーシートには、主として冷延鋼板
が使用されているが、燃費向上の観点から軽量化が求め
られ、アルミニウム合金板の採用が進められている。こ
の自動車ボディシートにはプレス加工による成形性が要
求されるため、アルミニウム合金の中でも強度および成
形性に優れる５０００系、すなわち、Ａｌ−Ｍｇ合金が
使用されている。ところが、Ａｌ−Ｍｇ合金は製造性が
悪いためにコストが高く、また、リューダースマークが
発生しやすいため、成形後、良好な表面性状が得られ難
い。そこで、製造コストが安く、リューダースマークを
生じない６０００系、すなわち、Ａｌ−Ｍｇ−Ｓｉを用
いることが望ましいため、開発が進められている。2. Description of the Related Art Applications requiring high moldability and high strength,
For example, cold rolled steel sheets are mainly used for body sheets of automobiles, but weight reduction is required from the viewpoint of improving fuel efficiency, and aluminum alloy sheets are being used. Since the formability by press working is required for this automobile body sheet, 5000 series which is excellent in strength and formability among aluminum alloys, that is, Al-Mg alloy is used. However, Al-Mg alloys have a high cost due to poor manufacturability, and are liable to generate Rudersmark, so that it is difficult to obtain good surface properties after molding. Therefore, it is desirable to use the 6000 series, which has a low production cost and does not generate Ruder's mark, that is, Al-Mg-Si, and therefore, development is proceeding.
【０００３】[0003]
【発明が解決しようとする課題】しかし、Ａｌ−Ｍｇ−
Ｓｉ系合金はＡｌ−Ｍｇ系合金に比べて成形性が劣って
いる。これは、Ａｌ−Ｍｇ−Ｓｉ系合金が析出強化によ
り高強度を得られる合金であり、塗装焼き付け後の強度
上昇、いわゆるＢＨ性に優れる反面、製造時に析出物を
生じ易く、その析出物によって延性が低下するためであ
る。さらに、これまでは強度確保のためのＢＨ性を高め
る点に着目した、熱処理条件等の製造条件の検討が優先
的に行われており（例えば、特開平４−２５９３５８号
公報、特開平６−２０４２５９号公報等）、成形性の検
討は不十分である。However, Al-Mg-
The formability of the Si-based alloy is inferior to that of the Al-Mg-based alloy. This is an alloy in which an Al-Mg-Si-based alloy can obtain high strength by precipitation strengthening. The strength is increased after baking, so-called BH property is excellent, but a precipitate is easily generated at the time of production, and ductility is caused by the precipitate. Is to be reduced. Further, a study of manufacturing conditions such as a heat treatment condition has been prioritized with a focus on enhancing the BH property for securing the strength (for example, JP-A-4-259358 and JP-A-6-259358). 204259), the study of moldability is insufficient.
【０００４】この課題に対してＣｕの添加により成形性
を向上させるという手段がある。しかし、Ｃｕの添加に
より成形性は向上するが、耐食性が低下するため、自動
車ボディーシートに用いる際には、特に耐糸錆性が問題
である。本発明はＡｌ−Ｍｇ−Ｓｉ系にＣｕを添加して
成形性を向上させ、さらにはＣｕ添加による耐食性の低
下を防止した、高ＢＨ性を有するＡｌ−Ｍｇ−Ｓｉ−Ｃ
ｕ系合金を提供するものである。[0004] To solve this problem, there is a method of improving the formability by adding Cu. However, although the moldability is improved by the addition of Cu, the corrosion resistance is deteriorated. Therefore, when used for an automobile body sheet, the rust resistance is particularly problematic. The present invention improves the formability by adding Cu to an Al-Mg-Si system, and further prevents Al-Mg-Si-C having a high BH property from preventing a decrease in corrosion resistance due to the addition of Cu.
It provides a u-based alloy.
【０００５】[0005]
【発明を解決するための手段】本発明者は前述の課題を
解決するために詳細な検討を重ね、Ｃｕ添加による耐食
性の低下が結晶粒界に生じたＣｕ系析出物であることを
明らかにし、この析出物の制御により、ＢＨ性、成形性
および耐食性の兼備が可能であることを見いだした。さ
らに、成分系、特にＭｇとＣｕ量を限定し、さらに好ま
しくは製造条件、特に溶体化処理後の冷却速度の下限を
限定することによってＣｕ系析出物のサイズおよび析出
状態を制御し、成形性にも耐食性にも優れた、ＢＨ性の
高いＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金を発明するに至っ
た。The present inventors have conducted detailed studies in order to solve the above-mentioned problems, and have clarified that the decrease in corrosion resistance due to the addition of Cu is caused by Cu-based precipitates generated at crystal grain boundaries. It has been found that by controlling the precipitates, it is possible to achieve both BH property, formability and corrosion resistance. Furthermore, the size and the state of the Cu-based precipitates are controlled by limiting the component systems, particularly the amounts of Mg and Cu, and more preferably by limiting the lower limit of the cooling rate after the solution treatment, particularly the production conditions, and Al-Mg-Si-Cu based alloys having excellent BH properties and excellent corrosion resistance have been invented.
【０００６】すなわち、本発明の要旨とするところは、 （１）重量％で、Ｍｇ：０．１〜０．６５％、Ｓｉ：
０．４〜２％、Ｃｕ：０．８〜１．４％、Ｍｇ＋Ｃｕ：
０．９〜１．５％を含有し、Ｚｎ：０．０３〜１．５
％、Ｍｎ：０．０３〜０．２％、Ｃｒ：０．０３〜０．
２％、Ｚｒ：０．０３〜０．１５％、Ｖ：０．０３〜
０．１５％、Ｆｅ：０．０３〜０．３％、Ｔｉ：０．０
０５〜０．１％のうちの１種または２種以上を、さらに
含有し、残部はＡｌ及び不可避的不純物からなるＡｌ合
金であって、結晶粒界上のＣｕを含有する析出物の最大
径が０．５μｍ以下で、かつ、その結晶粒界面に占める
割合が５％以下であり、さらに、粒内に０．２μｍ以上
の最大径を有する晶析出物が、１００μｍ2 当たり２０
個未満であることを特徴とする耐食性および成形性に優
れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板。That is, the gist of the present invention is as follows: (1) Mg: 0.1 to 0.65%, Si:
0.4-2%, Cu: 0.8-1.4%, Mg + Cu:
0.9-1.5%, Zn: 0.03-1.5
%, Mn: 0.03 to 0.2%, Cr: 0.03 to 0.
2%, Zr: 0.03 to 0.15%, V: 0.03 to
0.15%, Fe: 0.03 to 0.3%, Ti: 0.0
The maximum diameter of a Cu-containing precipitate on a crystal grain boundary, which further contains one or more of 0.05 to 0.1%, and the balance is an Al alloy including Al and unavoidable impurities. Is 0.5 μm or less, and the proportion occupying the crystal grain interface is 5% or less, and crystal precipitates having a maximum diameter of 0.2 μm or more in the grains are 20 μm / 100 μm 2.
An Al-Mg-Si-Cu-based alloy plate excellent in corrosion resistance and formability, characterized in that the number is less than one.
【０００７】（２）前記（１）に記載のＡｌ−Ｍｇ−Ｓ
ｉ−Ｃｕ系合金板の製造方法であって、冷間圧延後の溶
体化処理を５２０℃以上で５分以下とし、溶体化処理後
の冷却を溶体化温度〜２００℃の温度域の冷却速度を１
５℃／ｓｅｃ超とすることを特徴とする耐食性および成
形性に優れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板の製造方
法。 （３）前記（１）に記載のＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合
金板の製造方法であって、熱間圧延後に２５０℃以上４
５０℃未満で０．５〜４時間の保持を施すことを特徴と
するＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板の製造方法。(2) Al-Mg-S as described in (1) above
A method for producing an i-Cu alloy sheet, wherein a solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and a cooling rate after the solution treatment is a cooling rate in a temperature range from a solution treatment temperature to 200 ° C. 1
A method for producing an Al-Mg-Si-Cu alloy sheet excellent in corrosion resistance and formability, characterized in that the temperature is higher than 5 ° C / sec. (3) The method for producing an Al-Mg-Si-Cu-based alloy sheet according to (1), wherein after hot rolling, the temperature is 250 ° C or higher.
A method for producing an Al-Mg-Si-Cu-based alloy sheet, wherein the sheet is held at a temperature lower than 50C for 0.5 to 4 hours.
【０００８】（４）前記（１）に記載のＡｌ−Ｍｇ−Ｓ
ｉ−Ｃｕ系合金板の製造方法であって、冷間圧延後の溶
体化処理を５２０℃以上で５分以下とし、溶体化処理後
の冷却を溶体化温度〜２００℃の温度域の冷却速度を１
５℃／ｓｅｃ超とし、４０〜１００℃で巻取った後、
０．１〜１０℃／ｈの冷却速度で冷却することを特徴と
する耐食性および成形性に優れたＡｌ−Ｍｇ−Ｓｉ−Ｃ
ｕ系合金板の製造方法。 （５）前記（１）に記載のＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合
金板の製造方法であって、冷間圧延後の溶体化処理を５
２０℃以上で５分以下とし、溶体化処理後の冷却を溶体
化温度〜２００℃の温度域の冷却速度を１５℃／ｓｅｃ
超とし、４０〜１００℃で巻取った後、４０〜１００℃
で０．５〜５０時間保持することを特徴とする耐食性お
よび成形性に優れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板の
製造方法。(4) Al-Mg-S as described in (1) above
A method for producing an i-Cu alloy sheet, wherein a solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and a cooling rate after the solution treatment is a cooling rate in a temperature range from a solution treatment temperature to 200 ° C. 1
After 5 ° C / sec or more and winding at 40 to 100 ° C,
Al-Mg-Si-C excellent in corrosion resistance and formability characterized by cooling at a cooling rate of 0.1 to 10 ° C / h.
A method for producing a u-based alloy plate. (5) The method for producing an Al-Mg-Si-Cu alloy sheet according to (1), wherein the solution treatment after the cold rolling is performed by 5
The cooling after the solution treatment is performed at a cooling rate of 15 ° C./sec in the temperature range from the solution temperature to 200 ° C.
After super winding and winding at 40-100 ° C, 40-100 ° C
The method for producing an Al-Mg-Si-Cu alloy sheet excellent in corrosion resistance and formability, characterized by holding for 0.5 to 50 hours.
【０００９】（６）前記（１）に記載のＡｌ−Ｍｇ−Ｓ
ｉ−Ｃｕ系合金板の製造方法であって、冷間圧延後の溶
体化処理を５２０℃以上で５分以下とし、溶体化処理後
の冷却を溶体化温度〜２００℃の温度域の冷却速度を１
５℃／ｓｅｃ超とし、４０〜１００℃で巻取った後、
０．１〜１０℃／ｈの冷却速度で冷却し、さらに１３０
〜２８０℃に加熱して０超〜３０分保持することを特徴
とする耐食性および成形性に優れたＡｌ−Ｍｇ−Ｓｉ−
Ｃｕ系合金板の製造方法。 （７）前記（１）に記載のＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合
金板を製造方法であって、冷間圧延後の溶体化処理を５
２０℃以上で５分以下とし、溶体化処理後の冷却を溶体
化温度〜２００℃の温度域の冷却速度を１５℃／ｓｅｃ
超とし、４０〜１００℃で巻取った後、０．１〜１０℃
／ｈの冷却速度で冷却し、さらに１３０〜２８０℃に加
熱して０超〜３０分保時した後、４０〜１００℃まで冷
却して巻取り、０．１〜１０℃／ｈの冷却速度で冷却す
ることを特徴とする耐食性および成形性に優れたＡｌ−
Ｍｇ−Ｓｉ−Ｃｕ系合金板の製造方法、である。(6) Al-Mg-S as described in (1) above
A method for producing an i-Cu alloy sheet, wherein a solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and a cooling rate after the solution treatment is a cooling rate in a temperature range from a solution treatment temperature to 200 ° C. 1
After 5 ° C / sec or more and winding at 40 to 100 ° C,
Cool at a cooling rate of 0.1 to 10 ° C / h, and further cool
Al-Mg-Si- excellent in corrosion resistance and moldability characterized in that it is heated to -280 ° C and held for more than 0 to 30 minutes.
A method for producing a Cu-based alloy plate. (7) The method for producing an Al-Mg-Si-Cu alloy plate according to (1), wherein the solution treatment after the cold rolling is performed by 5
The cooling after the solution treatment is performed at a cooling rate of 15 ° C./sec in the temperature range from the solution temperature to 200 ° C.
After super winding and winding at 40-100 ° C, 0.1-10 ° C
/ H, cooling to 130-280 ° C and keeping for more than 0-30 minutes, then cooling to 40-100 ° C and winding, cooling rate of 0.1-10 ° C / h Al- with excellent corrosion resistance and moldability characterized by cooling with
A method for producing an Mg—Si—Cu alloy plate.
【００１０】[0010]
【発明の実施の形態】以下に、本発明の合金組成や析出
物の析出状態、製造条件等の限定理由を具体的に説明す
る。 Ｍｇ：Ｍｇは本発明の合金系では基本となる合金元素で
あり、塗装焼き付け時にＭｇ−Ｓｉ系の微細な析出物を
生じて高ＢＨ性の発現に寄与するものである。しかし、
Ｍｇ量が０．１％未満ではＢＨ性が不十分ではなく、一
方、０．６５％を超える過剰な添加により結晶粒界に粗
大なＭｇ−Ｓｉ―Ｃｕ系析出物を生じ、耐食性および成
形性を低下させる。このことから、Ｍｇ量は０．１〜
０．６５％の範囲とする。BEST MODE FOR CARRYING OUT THE INVENTION The reasons for limiting the alloy composition, the precipitation state of precipitates, the production conditions and the like according to the present invention will be specifically described below. Mg: Mg is a basic alloying element in the alloy system of the present invention, and contributes to the manifestation of high BH properties by generating Mg-Si based fine precipitates during baking. But,
When the amount of Mg is less than 0.1%, the BH property is not insufficient. On the other hand, an excessive addition exceeding 0.65% produces coarse Mg-Si-Cu-based precipitates at the crystal grain boundaries, resulting in corrosion resistance and formability. Lower. From this, the amount of Mg is 0.1 to
The range is 0.65%.
【００１１】Ｓｉ：Ｓｉも本発明の合金系では基本とな
る合金元素であり、塗装焼き付け時にＭｇ−Ｓｉ系の微
細な析出物を生じて高ＢＨ性の発現に寄与するが、Ｓｉ
量が０．４％未満ではＢＨ性が不十分であり、一方、２
％を超えると粗大なＳｉ相が析出して成形性を低下させ
る。このことから、Ｓｉ量は０．４〜２％の範囲とす
る。Si: Si is also a basic alloying element in the alloy system of the present invention, and contributes to the development of high BH property by generating Mg-Si based fine precipitates during baking.
When the amount is less than 0.4%, the BH property is insufficient.
%, A coarse Si phase is precipitated to lower the formability. For this reason, the amount of Si is set in the range of 0.4 to 2%.
【００１２】Ｃｕ：Ｃｕも本発明の合金系では基本とな
る合金元素であり、成形性を向上させるが、Ｃｕ量が
０．８％未満では十分な成形性が確保できず、一方、
１．４％を超える過剰な添加により結晶粒界に粗大なＡ
ｌ−Ｍｇ−Ｓｉ―Ｃｕ系析出物を生じ、耐食性および成
形性を低下させる。このことから、Ｃｕ量は０．８〜
１．４％の範囲とする。さらに、Ｍｇ＋Ｃｕが０．９％
未満ではＢＨ性および成形性が不十分であり、１．５％
を超えると通常の溶体化処理条件ではＡｌ−Ｍｇ−Ｓｉ
―Ｃｕ系析出物の生成を抑制できなくなり、耐食性およ
び成形性が低下することから、Ｍｇ＋Ｃｕを０．９〜
１．５％の範囲とする。[0012] Cu: Cu is also a basic alloying element in the alloy system of the present invention, and improves the formability. However, if the Cu content is less than 0.8%, sufficient formability cannot be ensured.
Coarse A at the grain boundaries due to excessive addition exceeding 1.4%
1-Mg-Si-Cu-based precipitates are formed, and the corrosion resistance and the formability are reduced. From this, the Cu content is 0.8 to
It is in the range of 1.4%. Furthermore, 0.9% of Mg + Cu
If it is less than 1.5%, the BH property and moldability are insufficient, and
Is exceeded, the Al-Mg-Si under normal solution treatment conditions
-Since the formation of Cu-based precipitates cannot be suppressed and the corrosion resistance and moldability are reduced, Mg + Cu is reduced to 0.9 to 0.9%.
The range is 1.5%.
【００１３】Ｚｎ，Ｍｎ，Ｃｒ，Ｚｒ，Ｖ，Ｔｉ，Ｆ
ｅ：これらの元素は強度向上や結晶粒微細化のために１
種または２種以上添加される。これらのうち、Ｚｎは合
金の時効性の向上を通じて強度向上に寄与する元素であ
り、その含有量が０．０３％未満では上記の効果が不十
分であり、一方、１．５％を超えれば成形性および耐食
性が低下する。従ってＺｎを添加する場合のＺｎの量は
０．０３〜１．５％の範囲内とした。Zn, Mn, Cr, Zr, V, Ti, F
e: These elements are used for improving strength and refining crystal grains.
Seeds or two or more are added. Of these, Zn is an element that contributes to the strength improvement through the improvement of the aging property of the alloy. If its content is less than 0.03%, the above-mentioned effects are insufficient, while if it exceeds 1.5%, Moldability and corrosion resistance decrease. Therefore, when Zn is added, the amount of Zn is set in the range of 0.03 to 1.5%.
【００１４】さらにＭｎ，Ｃｒ，Ｚｒ，Ｖは強度向上と
結晶粒の微細化に効果のある元素であり、いずれも含有
量が０．０３％未満では上記の効果が十分に得られな
い。一方、Ｍｎ，Ｃｒは０．２％を、Ｚｒは０．１５％
を、Ｖは０．１％を超えると巨大金属間化合物を生じて
成形性を低下させる。したがって、Ｍｎは０．０３〜
０．２％、Ｃｒは０．０３〜０．２％、Ｚｒは０．０３
〜０．１５％、Ｖは０．０３〜０．１５％の範囲とし
た。Further, Mn, Cr, Zr, and V are elements that are effective in improving the strength and refining the crystal grains. If the content is less than 0.03%, the above effects cannot be sufficiently obtained. On the other hand, Mn and Cr are 0.2% and Zr is 0.15%.
When V exceeds 0.1%, a large intermetallic compound is formed to lower the moldability. Therefore, Mn is 0.03 to
0.2%, Cr is 0.03-0.2%, Zr is 0.03
Ｖ0.15%, and V was in the range of 0.03〜0.15%.
【００１５】また、Ｆｅも強度向上と鋳塊組織の微細化
に有効な元素であり、その含有量が０．０３％未満では
十分な効果が得られず、０．３％を超えれば巨大晶出物
を生じて成形性を低下させるため、Ｆｅ量は０．０３〜
０．３％とした。Ｔｉも強度向上と鋳塊組織の微細化に
有効な元素であり、その含有量が０．００５％未満では
十分な効果が得られず、０．１％を超えれば巨大晶出物
を生じて成形性を低下させるため、Ｔｉ量は０．００５
〜０．１％とした。なお、これらのＺｎ、Ｍｎ、Ｃｒ、
Ｚｒ、Ｖ、Ｆｅ、Ｔｉの範囲は積極的な添加元素として
これらの元素を含む場合を示したものであり、いずれも
その下限値よりも少ない量を不純物として含有すること
は特に支障ない。Further, Fe is also an element effective for improving the strength and refining the ingot structure. If its content is less than 0.03%, a sufficient effect cannot be obtained. The amount of Fe is 0.03-
0.3%. Ti is also an element effective for improving the strength and refining the ingot structure. If the content is less than 0.005%, a sufficient effect cannot be obtained. If the content exceeds 0.1%, a giant crystal is generated. To reduce the formability, the Ti content is 0.005.
To 0.1%. In addition, these Zn, Mn, Cr,
The ranges of Zr, V, Fe, and Ti show the cases where these elements are included as positively added elements, and it is not particularly hindered to include any of the elements in an amount smaller than the lower limit as an impurity.
【００１６】次に、本発明における合金板に析出するＣ
ｕ系析出物およびのサイズ、析出状態について説明す
る。成形性および耐食性に影響を及ぼす析出物はその大
きさと析出する場所および分布状態に依存する。すなわ
ち、Ｃｕ系析出物が結晶粒界上にあり、その最大径が
０．５μｍ以上であれば、あるいは、最大径が０．５μ
ｍ以下であっても結晶粒界を占める割合が５％を超える
状態であれば、結晶粒界に沿った割れを生じやすくなり
成形性が低下する。また、結晶粒界上に上述の分布状態
でＣｕ系析出物が生じればその周囲のＣｕ量が減少する
ため、粒界腐食、すなわち、糸錆が発生し易くなる。Next, C deposited on the alloy sheet in the present invention
The size and the state of precipitation of the u-based precipitate will be described. Precipitates that affect formability and corrosion resistance depend on the size, location and distribution of the precipitates. That is, if the Cu-based precipitate is on the crystal grain boundary and the maximum diameter is 0.5 μm or more, or the maximum diameter is 0.5 μm.
If the ratio occupying the crystal grain boundary exceeds 5% even if it is less than m, cracks are likely to occur along the crystal grain boundary, and the formability decreases. In addition, if Cu-based precipitates are formed in the above-mentioned distribution state on the crystal grain boundaries, the amount of Cu around the precipitates is reduced, so that intergranular corrosion, that is, thread rust, is likely to occur.
【００１７】また、晶析出物が結晶粒内にある場合は、
その最大径が０．２μｍ以上の析出物が１００μｍ2 内
に２０個以上検出できる状態では破断の起点が多くな
り、成形性が低下する。したがって、冷延板の晶析出物
の晶析出状態を前述のように規定する。なお、結晶粒界
のＣｕ系析出物および結晶粒内の晶析出物の析出状態
は、透過型電子顕微鏡を用いて５０００倍程度の倍率で
任意の５視野を撮影し、その写真からサイズを観察する
ことができる。When the crystal precipitate is in the crystal grain,
When 20 or more precipitates having a maximum diameter of 0.2 μm or more can be detected in 100 μm 2 , the number of starting points of fracture increases, and the formability decreases. Therefore, the crystal precipitation state of the crystal precipitate of the cold rolled sheet is specified as described above. In addition, the precipitation state of the Cu-based precipitates in the crystal grain boundaries and the crystal precipitates in the crystal grains can be determined by photographing any five visual fields at a magnification of about 5000 times using a transmission electron microscope and observing the size from the photograph. can do.
【００１８】さらに、前述の析出物を確保するための製
造条件について説明する。熱延板を製造するまでの工程
は、従来の一般的なＪＩＳ６０００系合金と同様でよ
い。すなわち、ＤＣ鋳造または連続鋳造などの方法によ
り鋳塊とし、均質化処理を施し必要に応じて表面研削を
行い、引き続き熱間圧延、冷間圧延し、溶体化処理を施
す工程から成るものである。溶体化温度は５２０℃未満
では十分に添加元素が固溶せず、結晶粒界に最大径が
０．５μｍ以上のＣｕ系析出物が析出し、さらに析出物
が結晶粒界を占める割合が５％を超える状態になり、あ
るいは結晶粒内に最大径が０．２μｍ以上の析出物が１
００μｍ2 内に２０個以上検出できる状態になり好まし
くない。また、このような溶体化処理は連続焼鈍炉で行
うことが一般的であり、処理時間が５分を超えることは
通板速度を遅くすることを意味し、生産性を著しく低下
させる。従って溶体化処理時間は５分以下とする。Further, production conditions for securing the above-mentioned precipitate will be described. The steps up to the production of the hot rolled sheet may be the same as those of a conventional general JIS 6000 series alloy. That is, the method comprises a step of forming an ingot by a method such as DC casting or continuous casting, performing homogenization treatment, performing surface grinding as necessary, and subsequently performing hot rolling, cold rolling, and solution treatment. . When the solution temperature is lower than 520 ° C., the added element does not form a solid solution sufficiently, and a Cu-based precipitate having a maximum diameter of 0.5 μm or more precipitates at the crystal grain boundary. % Or a precipitate having a maximum diameter of 0.2 μm or more in a crystal grain.
20 or more can be detected within 00 μm 2 , which is not preferable. Further, such a solution treatment is generally performed in a continuous annealing furnace, and if the treatment time exceeds 5 minutes, it means that the sheet passing speed is reduced, and the productivity is significantly reduced. Therefore, the solution treatment time is set to 5 minutes or less.
【００１９】また、溶体化処理後の溶体化温度から２０
０℃までの冷却速度は、冷却中の析出を抑制するために
１５℃／ｓｅｃ超であることが必要である。これよりも
遅いと冷却中に結晶粒界に最大径が０．５μｍ以上のＣ
ｕ系析出物が析出し、または析出物が結晶粒界を占める
割合が５％を超える状態になり、あるいは結晶粒内に最
大径が０．２μｍ以上の析出物が１００μｍ2 内に２０
個以上検出できる状態になり好ましくない。従って溶体
化処理後の冷却を溶体化温度〜２００℃の温度域の冷却
速度を１５℃／ｓｅｃ超とする。溶体化処理後は室温時
効を抑制し、高ＢＨ性を得るために速やかに１００℃程
度で数時間の安定化処理を施すことが有効である。Further, the solution temperature is set at 20% from the solution temperature after the solution treatment.
The cooling rate to 0 ° C. needs to be higher than 15 ° C./sec in order to suppress precipitation during cooling. If it is slower than this, C having a maximum diameter of 0.5 μm or more is
u-based precipitates are precipitated, or the proportion of the precipitates occupying the crystal grain boundary exceeds 5%, or precipitates having a maximum diameter of 0.2 μm or more in crystal grains are contained in 100 μm 2 .
This is not preferable because more than one can be detected. Therefore, the cooling rate after the solution treatment is set to a cooling rate of more than 15 ° C./sec in a temperature range from the solution treatment temperature to 200 ° C. After the solution treatment, it is effective to immediately perform stabilization treatment at about 100 ° C. for several hours in order to suppress aging at room temperature and obtain high BH property.
【００２０】また、冷延前あるいは冷延途中において中
間焼鈍を施すことも析出物の析出状態を制御する方法と
して有効である。すなわち、中間焼鈍によりＣｕ系析出
物を生成させ、溶体化処理時の析出物の再固溶を抑制す
ることにより、溶体化処理後の冷却時の析出を制御する
方法である。この時の熱処理条件として２５０℃未満で
は微細な析出物の粒界析出を抑制する効果が小さく、４
５０℃を超えると粗大な析出物を生じて溶体化処理時に
再固溶させることができなくなる。そのため、十分な過
飽和固溶体を得られなくなり、その結果、成形性および
ＢＨ性を低下させる。Further, intermediate annealing before or during cold rolling is also effective as a method for controlling the precipitation state of precipitates. That is, this is a method of controlling precipitation during cooling after solution treatment by generating Cu-based precipitates by intermediate annealing and suppressing re-dissolution of precipitates during solution treatment. If the heat treatment conditions at this time are lower than 250 ° C., the effect of suppressing the grain boundary precipitation of fine precipitates is small,
If the temperature is higher than 50 ° C., coarse precipitates are formed and cannot be solid-dissolved again during the solution treatment. Therefore, a sufficient supersaturated solid solution cannot be obtained, and as a result, moldability and BH property are reduced.
【００２１】また、２５０℃以上４５０℃以下の温度で
焼鈍しても、その焼鈍時間が０．５時間未満では溶体化
処理後の冷却中の粒界析出を抑制する効果が小さい。一
方、４時間を超えると粗大な析出物を生じて溶体化処理
時に再固溶させることができなくなるため、十分な過飽
和固溶体を得られなくなり、その結果、成形性およびＢ
Ｈ性を低下させる。したがって、熱処理条件を２５０℃
以上４５０℃以下で０．５時間以上４時間以下とする。
上記の熱処理を施すことにより結晶粒界上に析出する析
出物を制御すれば、冷延後の溶体化処理条件を緩和させ
ることが可能になる。Further, even when annealing at a temperature of 250 ° C. or more and 450 ° C. or less, if the annealing time is less than 0.5 hour, the effect of suppressing grain boundary precipitation during cooling after the solution treatment is small. On the other hand, if it exceeds 4 hours, coarse precipitates are formed and cannot be dissolved again during the solution treatment, so that a sufficient supersaturated solid solution cannot be obtained. As a result, moldability and B
Reduces H properties. Therefore, the heat treatment condition is set to 250 ° C.
The temperature is set to be not less than 450 ° C. and not more than 0.5 hours and not more than 4 hours.
By controlling the precipitates precipitated on the crystal grain boundaries by performing the above heat treatment, it becomes possible to relax the conditions for the solution treatment after cold rolling.
【００２２】さらに、溶体化処理後の巻取り温度および
巻取り後の冷却速度の制御によってＢＨ性を向上させる
ことが可能である。溶体化処理後、室温近傍で放置する
とクラスターの生成量が多くなり、塗装焼き付け時にＧ
Ｐゾーンの析出を妨げるため、ＢＨ性が低下する。これ
を防止するには４０℃以上の温度で巻取り、冷却中にＧ
Ｐゾーンを生成させることが有効である。しかしなが
ら、巻取り温度が１００℃を超えるとＧＰゾーンの生成
による耐力上昇が大きく、成形性が低下する。また、巻
取り後の冷却中に十分にＧＰゾーンを生成させ、ＢＨ性
の低下を抑制する必要があるが、冷却速度が速すぎて１
０℃／ｈを超えると、この効果が不十分である。逆に冷
却速度が遅すぎ、０．１℃／ｈ未満になると、ＧＰゾー
ンの生成による耐力上昇が大きく、成形性を阻害する。
従って、巻取り温度を４０〜１００℃の範囲とし、巻取
り後の冷却速度を０．１〜１０℃／ｈの範囲とする。Further, by controlling the winding temperature after the solution treatment and the cooling rate after the winding, the BH property can be improved. If left near room temperature after the solution treatment, the amount of clusters generated will increase.
Since the precipitation of the P zone is prevented, the BH property is reduced. To prevent this, wind at a temperature of 40 ° C or higher, and
It is effective to generate a P zone. However, if the winding temperature exceeds 100 ° C., the increase in proof stress due to the generation of the GP zone is large, and the formability decreases. In addition, it is necessary to sufficiently generate a GP zone during cooling after winding, and to suppress a decrease in BH properties.
If it exceeds 0 ° C./h, this effect is insufficient. Conversely, if the cooling rate is too slow and is less than 0.1 ° C./h, the increase in proof stress due to the generation of the GP zone is large, impairing the formability.
Therefore, the winding temperature is set in the range of 40 to 100 ° C, and the cooling rate after winding is set in the range of 0.1 to 10 ° C / h.
【００２３】また、上述の条件で巻取った後、冷却速度
を制御して室温まで冷却する代わりに、速やかにＧＰゾ
ーンを生成する温度範囲で熱処理を施すことによって、
ＢＨ性を向上させることが可能である。この熱処理温度
も、４０℃未満ではクラスターが多く生成してＢＨ性を
阻害し、１００℃を超えると耐力が増加して成形性が低
下する。また、時間は０．５時間未満ではＧＰゾーンの
生成が不十分であるため、その後の室温で放置するとク
ラスターを生じてＢＨ性が低下し、５０時間を超えると
耐力が上昇して成形性および曲げ性が低下する。従っ
て、熱処理温度は４０〜１００℃の範囲とし、熱処理時
間は０．５〜５０時間の範囲とする。Further, after winding under the above-mentioned conditions, instead of cooling to room temperature by controlling the cooling rate, heat treatment is performed in a temperature range in which a GP zone is quickly generated.
BH property can be improved. If the heat treatment temperature is lower than 40 ° C., a large number of clusters are formed to inhibit the BH property. If the heat treatment temperature is higher than 100 ° C., the yield strength increases and the formability decreases. If the time is less than 0.5 hour, the formation of the GP zone is insufficient, so that if left at room temperature thereafter, clusters are formed and the BH property is reduced. Flexibility decreases. Therefore, the heat treatment temperature is in the range of 40 to 100 ° C., and the heat treatment time is in the range of 0.5 to 50 hours.
【００２４】より高いＢＨ性を得るためには、溶体化処
理後に上述の条件で巻取り、冷却あるいは熱処理を行っ
た後、比較的高温かつ短時間の復元処理を行うことが有
効である。すなわち、溶体化処理後にＧＰゾーンを生成
させて、クラスターの生成を抑制し、さらに復元処理に
よってクラスターを溶解し、ＧＰゾーンを生成させるこ
とにより極めて高いＢＨ性が得られる。この際にも、溶
体化処理後の巻取り温度は、４０℃未満ではクラスター
が生成するため下限とし、１００℃を超えると耐力が増
加して成形性および曲げ性が低下するため上限とする。
また、冷却速度は０．１℃／ｈ未満では耐力が増加して
成形性および曲げ性が低下するため下限とし、１０℃／
ｈを超えるとＧＰゾーンの生成が不十分であり、その後
の室温で放置するとクラスターを生じてＢＨ性が低下す
るため上限とする。In order to obtain a higher BH property, it is effective to perform a rewinding treatment at a relatively high temperature and for a short time after winding, cooling or heat treatment under the above conditions after the solution treatment. That is, the generation of the GP zone after the solution treatment suppresses the generation of the cluster, and further, the cluster is dissolved by the restoring treatment to generate the GP zone, whereby an extremely high BH property is obtained. Also in this case, the winding temperature after the solution treatment is set to the lower limit when the temperature is lower than 40 ° C. because clusters are formed, and is set to the upper limit when the temperature is higher than 100 ° C. because the yield strength increases and the formability and bendability decrease.
If the cooling rate is less than 0.1 ° C./h, the yield strength is increased and the formability and bendability are reduced.
When h is exceeded, the generation of the GP zone is insufficient, and when left at room temperature thereafter, clusters are formed and the BH property is reduced, so the upper limit is set.
【００２５】なお、溶体化処理後、冷却して巻取り、速
やかに４０〜１００℃で０．５〜５０時間の熱処理を施
しても同等の効果が得られる。その後の復元処理は１３
０℃未満ではクラスターが溶解せずＧＰゾーンの析出が
生じるため、耐力が増加し、成形性および曲げ性を損な
う。また、２８０℃を超えると耐力が増加し、また、中
間相を生じて成形性および曲げ性が著しく低下する。ま
た、保持時間が３０分を超えると耐力が増加して成形性
および曲げ性を低下させる。従って、復元処理の温度範
囲は１３０〜２８０℃、保持時間は０超〜３０分とす
る。It is to be noted that the same effect can be obtained by cooling and winding after the solution treatment, and immediately performing a heat treatment at 40 to 100 ° C. for 0.5 to 50 hours. The restoring process is 13
If the temperature is lower than 0 ° C., the cluster does not dissolve and the GP zone is precipitated, so that the yield strength increases and the formability and bendability are impaired. On the other hand, when the temperature exceeds 280 ° C., the proof stress increases, and an intermediate phase is formed, so that the formability and the bendability are remarkably reduced. On the other hand, if the holding time exceeds 30 minutes, the proof stress increases, and the formability and the bendability decrease. Therefore, the temperature range of the restoration process is 130 to 280 ° C., and the holding time is more than 0 to 30 minutes.
【００２６】さらにＢＨ性を向上させるには、復元処理
後、ＧＰゾーンが生成する条件で巻取りおよび冷却を行
うことが有効である。すなわち、復元処理後のクラスタ
ーの析出を抑制すればＢＨ性の低下を防止することがで
きる。特に、２００℃以上の高温で復元処理を行うと、
クラスターの溶解が促進されて溶質の過飽和度が上が
り、冷却後に室温近傍で放置すると再びクラスターが生
成してＢＨ性が低下しやすい。これを防止するために、
溶体化処理後と同様に巻取り温度の範囲を４０〜１００
℃に、冷却速度の範囲を０．１〜１０℃／ｈとする。ま
た、復元処理後、溶体化処理後と同様に４０〜１００℃
の温度範囲で巻取り、４０〜１００℃で０．５〜５０時
間保持する熱処理を施すことにより同等の効果が得られ
る。In order to further improve the BH property, it is effective to perform winding and cooling under conditions that generate GP zones after the restoration processing. That is, if the precipitation of clusters after the restoration treatment is suppressed, a decrease in BH property can be prevented. In particular, when the restoration process is performed at a high temperature of 200 ° C. or more,
The dissolution of the clusters is promoted to increase the degree of supersaturation of the solute, and if left near room temperature after cooling, the clusters are formed again and the BH property tends to decrease. To prevent this,
As in the case after the solution treatment, the range of the winding temperature is set to 40 to 100.
The cooling rate range is 0.1 to 10 ° C / h. After the restoration treatment, the temperature is set to 40 to 100 ° C. in the same manner as after the solution treatment.
The same effect can be obtained by performing a heat treatment in which the film is wound at a temperature in the range described above and held at 40 to 100 ° C. for 0.5 to 50 hours.
【００２７】[0027]
【実施例】次に実施例に基づいて、本発明を具体的に説
明する。 （実施例１）表１に示すアルミニウム合金を、それぞれ
常法に従ってＤＣ鋳造法によって鋳造し、得られた鋳塊
に５３０℃×５ｈｒの均質化処理を施した後、熱間圧延
を行って熱延板とした。次いで５２０℃×１ｍｉｎの中
間焼鈍を施した後、厚さ１ｍｍの冷延板を製造し、５４
０℃×１０ｓｅｃの溶体化処理を施した。この時の５４
０℃〜２００℃間の冷却速度を１８℃／ｓｅｃとした。
さらに、溶体化処理後速やかに１００℃×３ｈｒの安定
化処理を施した。Next, the present invention will be specifically described based on examples. (Example 1) Each of the aluminum alloys shown in Table 1 was cast by a DC casting method according to a conventional method, and the obtained ingot was subjected to a homogenization treatment at 530 ° C for 5 hours, and then subjected to hot rolling. It was a rolled sheet. Next, after performing an intermediate annealing at 520 ° C. × 1 min, a cold-rolled sheet having a thickness of 1 mm was manufactured.
A solution treatment at 0 ° C. × 10 sec was performed. 54 at this time
The cooling rate between 0 ° C and 200 ° C was 18 ° C / sec.
Further, immediately after the solution treatment, a stabilization treatment at 100 ° C. × 3 hr was performed.
【００２８】[0028]
【表１】 [Table 1]
【００２９】以上の製造条件によって製造した冷延板の
析出状態を透過型電子顕微鏡を用いて、５０００倍の写
真を任意の場所で５視野撮影し、その範囲で観察される
析出物のサイズおよび数を測定し、評価した。機械的性
質のうち引張試験はこれらの合金板からＪＩＳ５号試験
片を切り出し、耐力測定までは１ｍｍ／ｍｉｎ、耐力測
定以降は１０ｍｍ／ｍｉｎの引張速度で行った。また、
ＢＨ性は引張試験片に１８０℃×２０ｍｉｎの熱処理を
施し、耐力を測定して評価した。The precipitation state of the cold-rolled sheet manufactured under the above manufacturing conditions was photographed by a transmission electron microscope at a magnification of 5000 at five arbitrary fields, and the size and size of the precipitate observed in the range were measured. The number was measured and evaluated. Among the mechanical properties, a tensile test was performed by cutting out JIS No. 5 test pieces from these alloy plates and performing a tensile speed of 1 mm / min until the proof stress measurement, and a 10 mm / min tensile speed after the proof stress measurement. Also,
The BH property was evaluated by subjecting a tensile test piece to heat treatment at 180 ° C. for 20 minutes and measuring the proof stress.
【００３０】プレス成形性評価には曲げ成形および張出
成形を行った。まず、曲げ試験はＪＩＳ３号試験片を切
り出し、０．５ｔの内側半径で１８０°曲げを行い、そ
の外側部分の外観観察を行って、割れが発生しなかった
ものを○、および割れが発生したものを×として評価し
た。張出成形性は１００φの球頭張出工具を用い、長さ
２００ｍｍ×幅１２５〜１４０ｍｍの試験片に対して潤
滑油を塗布した後に成形速度１０ｍｍ／ｍｉｎ、ＢＨＦ
１０トンで成形して破断成形高さ（ＬＤＨ０）を求め、
評価した。For press formability evaluation, bending and overhanging were performed. First, in the bending test, a JIS No. 3 test piece was cut out, bent 180 ° at an inner radius of 0.5 t, and the outer part was observed for appearance. Those were evaluated as x. The overhanging formability was determined by using a 100 mm ball-overhanging tool, applying a lubricating oil to a test piece having a length of 200 mm and a width of 125 to 140 mm, and forming at a molding speed of 10 mm / min.
10 tons to form and determine the break forming height (LDH0)
evaluated.
【００３１】耐食性は、脱脂、水洗、燐酸亜鉛処理、水
洗、塗装を行った試料表面にナイフで人工疵を入れた
後、塩水噴霧、湿潤した後、糸錆性を評価した。糸錆性
の評価は最大糸錆長さを基準として行い、１ｍｍ未満を
○、１ｍｍ以上を×とした。析出物の状態、機械的性
質、成形性、および耐食性を測定した結果を表２に示
す。本発明で示したＡ１〜Ａ１２の合金は規定範囲内の
析出状態で粒界を占める割合が少なく、伸びおよび曲げ
性に優れ、破断限界高さの高い成形性を有し、かつ高Ｂ
Ｈ性を有している。The corrosion resistance was evaluated by putting artificial flaws with a knife on the sample surface which had been degreased, washed with water, treated with zinc phosphate, washed with water, and painted, sprayed with salt water and wetted, and evaluated for rust resistance. The evaluation of the yarn rust property was based on the maximum length of the yarn rust, and the evaluation was as follows. Table 2 shows the results of measurement of the state of the precipitate, mechanical properties, moldability, and corrosion resistance. The alloys of A1 to A12 shown in the present invention have a small proportion occupying the grain boundaries in a precipitation state within a specified range, have excellent elongation and bendability, have high formability with a high breaking limit height, and have a high B
It has H property.
【００３２】[0032]
【表２】 [Table 2]
【００３３】一方、比較例で示した合金のうち、Ｂ１は
Ｍｇ量が少なく、Ｂ４はＳｉ量が少ないため、ＢＨ性が
不十分であり、Ｂ２はＭｇ量が多く、Ｂ５はＣｕ量が多
いため、結晶粒界にＣｕ系析出物を生じ、成形性および
耐食性が低下している。Ｂ３はＳｉ量が多いため、成形
性が低下しており、Ｂ６はＣｕ量が少ないため、成形性
が不十分である。さらに、比較例で示した他の合金は、
晶析出物を生じる成分が本発明で規定した範囲を外れて
おり、製造条件を本発明で規定した範囲内で製造したに
もかかわらず粒内の晶析出物の分布が本発明で規定する
範囲を外れ、その結果曲げ性および成形性が本発明より
著しく劣っている。On the other hand, among the alloys shown in the comparative examples, B1 has a small amount of Mg, B4 has a small amount of Si, so the BH property is insufficient, B2 has a large amount of Mg, and B5 has a large amount of Cu. Therefore, a Cu-based precipitate is generated at the crystal grain boundary, and the formability and the corrosion resistance are reduced. B3 has a large amount of Si and therefore has low formability, and B6 has a low Cu amount and therefore has insufficient formability. Further, other alloys shown in the comparative example,
The components that generate crystal precipitates are out of the range specified in the present invention, and the distribution of crystal precipitates in the grains is defined in the present invention even though the production conditions are manufactured within the range specified in the present invention. And, as a result, the bendability and formability are significantly inferior to those of the present invention.
【００３４】（実施例２）実施例１と同様に製造したＡ
４の本発明で規定した範囲内の合金熱延板を用いて表３
に示す条件の中間焼鈍を施して厚さ１ｍｍの冷延板を製
造した。これらの冷延板に表に示す溶体化処理を施して
実施例１と同様に析出状態を観察し、機械的性質、プレ
ス成形性および耐食性を評価し、表４に示した。表に示
す通り、本発明では溶体化処理条件を本発明範囲内で示
す条件で行うことにより、析出物が粒界を占める割合が
小さく、その結果伸びおよび曲げ性に優れ、高い成形性
を有しかつＢＨ性および耐食性に優れた合金板が得られ
た。Example 2 A manufactured in the same manner as in Example 1
Table 3 was obtained by using an alloy hot-rolled sheet within the range specified in the present invention of No. 4
The steel sheet was subjected to intermediate annealing under the following conditions to produce a cold-rolled sheet having a thickness of 1 mm. These cold-rolled sheets were subjected to the solution treatment shown in the table, and the precipitation state was observed in the same manner as in Example 1. The mechanical properties, press formability, and corrosion resistance were evaluated. As shown in the table, in the present invention, by performing the solution treatment under the conditions shown in the range of the present invention, the ratio of the precipitate occupying the grain boundary is small, and as a result, the precipitate has excellent elongation and bendability, and has high formability. Thus, an alloy plate excellent in BH property and corrosion resistance was obtained.
【００３５】[0035]
【表３】 [Table 3]
【００３６】[0036]
【表４】 [Table 4]
【００３７】一方、比較例のうちＮｏ．３０の場合は溶
体化処理温度が本発明で規定した温度より低く、粗大な
析出物が粒界に多数観察され、伸びおよび成形性が低下
している。また、比較例の内、Ｎｏ．３１の場合は溶体
化処理後の冷却速度が本発明で規定した条件より遅く、
冷却中に粒界に析出物が析出、粗大化したと考えられ、
粒界に析出物が多数観察され、伸び、成形性および耐食
性が低下している。On the other hand, of the comparative examples, In the case of No. 30, the solution treatment temperature is lower than the temperature specified in the present invention, a large number of coarse precipitates are observed at the grain boundaries, and the elongation and the formability are reduced. Also, among the comparative examples, No. In the case of 31, the cooling rate after the solution treatment is lower than the condition specified in the present invention,
It is considered that precipitates were precipitated at the grain boundaries during cooling and coarsened,
Many precipitates are observed at the grain boundaries, and elongation, formability and corrosion resistance are reduced.
【００３８】（実施例３）実施例１と同様に製造したＡ
４の本発明で規定した範囲内の合金熱延板を用いて表５
に示す条件の中間焼鈍を施して厚さ１ｍｍの冷延板を製
造した。これらの冷延板に表５に示す溶体化処理を施し
て実施例１と同様に析出状態を観察し、機械的性質、プ
レス成形性および耐食性を評価し、表６に示した。表６
に示す通り、本発明では中間焼鈍条件を本発明範囲内で
示す条件で行うことにより、析出物が粒界を占める割合
が小さく、その結果伸びおよび曲げ性に優れ、高い成形
性を有しかつＢＨ性および耐食性に優れた合金板が得ら
れた。Example 3 A produced in the same manner as in Example 1
Table 5 was obtained by using an alloy hot-rolled sheet within the range specified in the present invention of No. 4
The steel sheet was subjected to intermediate annealing under the following conditions to produce a cold-rolled sheet having a thickness of 1 mm. These cold-rolled sheets were subjected to a solution treatment shown in Table 5 and the precipitation state was observed in the same manner as in Example 1. The mechanical properties, press formability and corrosion resistance were evaluated. Table 6
As shown in the present invention, by performing the intermediate annealing conditions under the conditions shown in the range of the present invention, the ratio of the precipitate occupying the grain boundary is small, as a result, excellent in elongation and bendability, having high formability and An alloy plate having excellent BH properties and corrosion resistance was obtained.
【００３９】[0039]
【表５】 [Table 5]
【００４０】[0040]
【表６】 [Table 6]
【００４１】一方、比較例のうちＮｏ．３７およびＮ
ｏ．３８の場合は中間焼鈍温度が本発明で規定した温度
より低く、あるいは時間が短いため、析出物が中間焼鈍
中に十分に粗大化しなかったため、溶体化処理後に微細
な析出物だ生成し、伸び、成形性および耐食性が低下し
たと考えられる。また、Ｎｏ．３９およびＮｏ．４０は
中間焼鈍時間が長すぎるために、析出物が粗大化し、溶
体化処理による再固溶が不十分で粗大な析出物が粒界に
多数観察され、伸びおよび成形性が低下している。ま
た、Ｎｏ．４１の場合は中間焼鈍温度が高すぎるために
晶析出物の大部分が中間焼鈍時に再固溶し、溶体化処理
温度が低い条件では、析出を促進させる結果となり、粒
界に析出物が析出、粗大化したと考えられ、粒界に析出
物が多数観察され、伸び、成形性および耐食性が低下し
ている。On the other hand, among the comparative examples, No. 37 and N
o. In the case of No. 38, since the intermediate annealing temperature was lower than the temperature specified in the present invention or the time was short, the precipitate did not sufficiently coarsen during the intermediate annealing, so that a fine precipitate was formed after the solution treatment, and the elongation was increased. It is considered that moldability and corrosion resistance were reduced. In addition, No. 39 and no. In No. 40, since the intermediate annealing time was too long, the precipitates were coarsened, re-solid solution by the solution treatment was insufficient, and a large number of coarse precipitates were observed at the grain boundaries, and elongation and formability were reduced. In addition, No. In the case of 41, most of the crystal precipitates re-dissolved during the intermediate annealing because the intermediate annealing temperature was too high, and under the condition of low solution treatment temperature, the precipitation was promoted, and the precipitates were precipitated at the grain boundaries. It is considered to be coarse, and a large number of precipitates were observed at the grain boundaries, and elongation, formability and corrosion resistance were reduced.
【００４２】（実施例４）実施例１と同様に製造した、
Ａ４の本発明で規定した範囲内の合金熱延板に、表３Ｎ
ｏ．２７に示す条件の中間焼鈍を施して厚さ１ｍｍの冷
延板を製造し、表３Ｎｏ．２７に示す溶体化処理を施し
た。さらに、表７に示す条件で巻取り、室温近傍まで冷
却した後、これらの合金板の析出状態を観察し、機械的
性質、プレス成形性および耐食性を実施例１と同様に評
価し、表８に示した。表８に示す通り、本発明では溶体
化処理条件を本発明範囲内で示す条件で行うことによ
り、析出物が粒界を占める割合が小さく、その結果伸び
および曲げ性に優れ、高い成形性を有しかつＢＨ性およ
び耐食性に優れた合金板が得られた。(Example 4)
Table 3N shows the hot-rolled alloy sheets within the range specified in the present invention of A4.
o. No. 27 was subjected to intermediate annealing to produce a cold-rolled sheet having a thickness of 1 mm. A solution treatment shown in FIG. 27 was performed. Further, after winding under the conditions shown in Table 7 and cooling to near room temperature, the precipitation state of these alloy sheets was observed, and the mechanical properties, press formability, and corrosion resistance were evaluated in the same manner as in Example 1. It was shown to. As shown in Table 8, in the present invention, by performing the solution treatment under the conditions shown in the range of the present invention, the ratio of the precipitate occupying the grain boundary is small, and as a result, the precipitate has excellent elongation and bendability, and high formability is obtained. An alloy plate having excellent BH properties and corrosion resistance was obtained.
【００４３】[0043]
【表７】 [Table 7]
【００４４】[0044]
【表８】 [Table 8]
【００４５】一方、比較例の内、Ｎｏ．４６の場合は巻
取り温度が本発明で規定した温度より低いため、冷却中
にクラスターを生じてＢＨ性が低下した。一方、Ｎｏ．
４７の場合は巻取り温度が本発明で規定した温度より高
いため、冷却中にＧＰゾーンを生じて耐力が上昇し、曲
げ性が低下した。また、Ｎｏ．４８の場合は巻取り後の
冷却速度が速すぎるために、冷却中のＧＰゾーンの析出
が不十分でクラスターを生じ、ＢＨ性が低下している。
一方、Ｎｏ．４９の場合は巻取り後の冷却速度が遅すぎ
るため、冷却中にＧＰゾーンを生じて耐力が上昇し、曲
げ性が低下している。On the other hand, among the comparative examples, No. In the case of No. 46, since the winding temperature was lower than the temperature specified in the present invention, clusters were formed during cooling and the BH property was lowered. On the other hand, No.
In the case of No. 47, since the winding temperature was higher than the temperature specified in the present invention, a GP zone was generated during cooling, the proof stress increased, and the bendability decreased. In addition, No. In the case of No. 48, since the cooling rate after winding was too high, the precipitation of the GP zone during cooling was insufficient and clusters were formed, and the BH property was lowered.
On the other hand, No. In the case of 49, since the cooling rate after winding is too slow, a GP zone is generated during cooling, the proof stress increases, and the bendability decreases.
【００４６】（実施例５）実施例１と同様に製造した、
Ａ４の本発明で規定した範囲内の合金熱延板に、表３Ｎ
ｏ．２７に示す条件の中間焼鈍を施して厚さ１ｍｍの冷
延板を製造し、表３Ｎｏ．２７に示す溶体化処理を施し
た。さらに、表９に示す条件で巻取り、速やかに熱処理
を施し、これらの合金板の析出状態を観察し、機械的性
質、プレス成形性および耐食性を実施例１と同様に評価
し、表１０に示した。表１０に示す通り、本発明では溶
体化処理条件を本発明範囲内で示す条件で行うことによ
り、析出物が粒界を占める割合が小さく、その結果伸び
および曲げ性に優れ、高い成形性を有しかつＢＨ性およ
び耐食性に優れた合金板が得られた。(Example 5)
Table 3N shows the hot-rolled alloy sheets within the range specified in the present invention of A4.
o. No. 27 was subjected to intermediate annealing to produce a cold-rolled sheet having a thickness of 1 mm. A solution treatment shown in FIG. 27 was performed. Further, it was wound up under the conditions shown in Table 9 and immediately subjected to heat treatment. The precipitation state of these alloy sheets was observed, and the mechanical properties, press formability and corrosion resistance were evaluated in the same manner as in Example 1. Indicated. As shown in Table 10, in the present invention, by performing the solution treatment under the conditions shown in the range of the present invention, the ratio of the precipitate occupying the grain boundary is small, and as a result, the elongation and bendability are excellent, and the high formability is improved. An alloy plate having excellent BH properties and corrosion resistance was obtained.
【００４７】[0047]
【表９】 [Table 9]
【００４８】[0048]
【表１０】 [Table 10]
【００４９】一方、比較例の内、Ｎｏ．５４の場合は熱
処理温度が本発明で規定した温度より低いため、クラス
ターを生じてＢＨ性が低下、Ｎｏ．５５の場合は熱処理
温度が本発明で規定した温度より高いため、ＧＰゾーン
を生じて耐力が上昇し、曲げ性が低下した。また、Ｎ
ｏ．５６の場合は熱処理時間が短いために、ＧＰゾーン
の析出が不十分でクラスターを生じ、ＢＨ性が低下して
いる。一方、Ｎｏ．５７の場合は熱処理時間が長すぎる
ため、ＧＰゾーンを生じて耐力が上昇し、曲げ性が低下
している。On the other hand, among the comparative examples, no. In the case of No. 54, since the heat treatment temperature was lower than the temperature specified in the present invention, clusters were generated and the BH property was reduced. In the case of No. 55, since the heat treatment temperature was higher than the temperature specified in the present invention, a GP zone was generated, the proof stress increased, and the bendability decreased. Also, N
o. In the case of No. 56, since the heat treatment time was short, the precipitation of the GP zone was insufficient, clusters were formed, and the BH property was lowered. On the other hand, No. In the case of No. 57, since the heat treatment time is too long, a GP zone is generated, the proof stress increases, and the bendability decreases.
【００５０】（実施例６）実施例１と同様に製造したＡ
４の本発明で規定した範囲内の合金熱延板に表３Ｎｏ．
２７に示す条件の中間焼鈍を施して厚さ１ｍｍの冷延板
を製造した。さらに、表３Ｎｏ．２７に示す溶体化処理
を施した後、表７製造番号４２に示す条件で巻取って室
温近傍まで冷却し、表１１に示す復元処理を施した。そ
の後、実施例１と同様にこれらの析出状態を観察し、機
械的性質、プレス成形性および耐食性を評価し、表１２
に示した。表に示す通り、本発明では溶体化処理条件を
本発明範囲内で示す条件で行うことにより、析出物が粒
界を占める割合が小さく、その結果伸びおよび曲げ性に
優れ、高い成形性を有しかつＢＨ性および耐食性に優れ
た合金板が得られた。Example 6 A manufactured in the same manner as in Example 1
No. 4 in Table 3 No. 4 was added to the hot-rolled alloy sheet within the range specified in the present invention.
Intermediate annealing under the conditions shown in No. 27 was performed to produce a cold-rolled sheet having a thickness of 1 mm. Further, Table 3 No. After performing the solution treatment shown in Table 27, the film was wound under the conditions shown in Table 7 production number 42, cooled to near room temperature, and subjected to a restoration treatment shown in Table 11. Thereafter, the precipitation state was observed in the same manner as in Example 1, and the mechanical properties, press formability, and corrosion resistance were evaluated.
It was shown to. As shown in the table, in the present invention, by performing the solution treatment under the conditions shown in the range of the present invention, the ratio of the precipitate occupying the grain boundary is small, and as a result, the precipitate has excellent elongation and bendability, and has high formability. Thus, an alloy plate excellent in BH property and corrosion resistance was obtained.
【００５１】[0051]
【表１１】 [Table 11]
【００５２】[0052]
【表１２】 [Table 12]
【００５３】一方、比較例の内、Ｎｏ．６２の場合は熱
処理温度が本発明で規定した温度より低いため、クラス
ターが溶解せずにＧＰゾーンが生成し、耐力が上昇して
成形性および曲げ性が低下した。一方、Ｎｏ．６３の場
合は熱処理温度が本発明で規定した温度より高いため、
耐力が上昇し、成形性および曲げ性が低下した。また、
Ｎｏ．６４の場合は熱処理時間が長すぎるために、ＧＰ
ゾーンを生じて耐力が上昇し、曲げ性が低下している。On the other hand, among the comparative examples, In the case of No. 62, since the heat treatment temperature was lower than the temperature specified in the present invention, the GP zone was generated without dissolving the cluster, the proof stress was increased, and the formability and the bendability were reduced. On the other hand, No. In the case of 63, since the heat treatment temperature is higher than the temperature specified in the present invention,
The yield strength increased, and the formability and bendability decreased. Also,
No. In the case of 64, the heat treatment time is too long.
Zones are generated, the proof stress increases, and the bendability decreases.
【００５４】（実施例７）実施例１と同様に製造した、
Ａ４の本発明で規定した範囲内の合金熱延板に表３Ｎ
ｏ．２７に示す条件の中間焼鈍を施して厚さ１ｍｍの冷
延板を製造した。さらに表３Ｎｏ．２７に示す溶体化処
理を施した後、表７Ｎｏ．４２に示す条件で巻取って室
温近傍まで冷却し、表１１Ｎｏ．６０に示す条件で復元
処理を施した。その後、表１３に示す条件で巻取って室
温近傍まで冷却し、実施例１と同様にこれらの析出状態
を観察し、機械的性質、プレス成形性および耐食性を評
価し、表１４に示した。表に示す通り、本発明では溶体
化処理条件を本発明範囲内で示す条件で行うことによ
り、析出物が粒界を占める割合が小さく、その結果伸び
および曲げ性に優れ、高い成形性を有しかつＢＨ性およ
び耐食性に優れた合金板が得られた。(Example 7)
Table 3N shows the hot-rolled alloy sheets within the range specified in the present invention for A4.
o. Intermediate annealing under the conditions shown in No. 27 was performed to produce a cold-rolled sheet having a thickness of 1 mm. Further, in Table 3 No. After performing the solution treatment shown in FIG. 42, and was cooled to around room temperature. The restoration process was performed under the conditions shown in FIG. Thereafter, it was wound up under the conditions shown in Table 13 and cooled to around room temperature. The precipitation state was observed in the same manner as in Example 1, and the mechanical properties, press formability and corrosion resistance were evaluated. As shown in the table, in the present invention, by performing the solution treatment under the conditions shown in the range of the present invention, the ratio of the precipitate occupying the grain boundary is small, and as a result, the precipitate has excellent elongation and bendability, and has high formability. Thus, an alloy plate excellent in BH property and corrosion resistance was obtained.
【００５５】[0055]
【表１３】 [Table 13]
【００５６】[0056]
【表１４】 [Table 14]
【００５７】一方、比較例の内、Ｎｏ．６９の場合は巻
取り温度が本発明で規定した温度より低いため、冷却中
にクラスターを生じ、本発明に比べてＢＨ性が低い。一
方、Ｎｏ．７０の場合は巻取り温度が本発明で規定した
温度より高いため、冷却中にＧＰゾーンを生じて耐力が
上昇し、曲げ性が低下した。また、Ｎｏ．７１の場合は
巻取り後の冷却速度が速すぎるためにクラスターを生
じ、本発明に比べてＢＨ性が低下している。一方、Ｎ
ｏ．７２の場合は巻取り後の冷却速度が遅すぎるため、
耐力が上昇し、曲げ性が低下している。On the other hand, among the comparative examples, no. In the case of 69, since the winding temperature is lower than the temperature specified in the present invention, clusters are formed during cooling, and the BH property is lower than in the present invention. On the other hand, No. In the case of 70, since the winding temperature was higher than the temperature specified in the present invention, a GP zone was generated during cooling, the proof stress increased, and the bendability decreased. In addition, No. In the case of 71, the cooling rate after winding was too high, clusters were formed, and the BH property was lower than that of the present invention. On the other hand, N
o. In the case of 72, the cooling rate after winding is too slow,
The proof stress increases and the bendability decreases.
【００５８】[0058]
【発明の効果】以上のように、本発明によれば、成形性
および耐食性に優れた高ＢＨ性を有する成形加工用アル
ミニウム合金板を提供できる。As described above, according to the present invention, it is possible to provide an aluminum alloy sheet for forming and processing having high BH property and excellent in formability and corrosion resistance.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｆ 1/00 ６２３ Ｃ２２Ｆ 1/00 ６２３ ６３０ ６３０Ｋ ６４０ ６４０Ａ ６８４ ６８４Ｃ ６９１ ６９１Ｂ ６９１Ｃ ６９２ ６９２Ａ ６９２Ｂ ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme court ゛ (Reference) C22F 1/00 623 C22F 1/00 623 630 630K 640 640A 684 684C 691 691B 691C 692 692A 692B
Claims (7)
Ａｌ及び不可避的不純物からなるＡｌ合金であって、結
晶粒界上のＣｕを含有する析出物の最大径が０．５μｍ
以下で、かつ、その結晶粒界面に占める割合が５％以下
であり、さらに、粒内に０．２μｍ以上の最大径を有す
る晶析出物が、１００μｍ2 当たり２０個未満であるこ
とを特徴とする耐食性および成形性に優れたＡｌ−Ｍｇ
−Ｓｉ−Ｃｕ系合金板。1. Mg: 0.1 to 0.65%, Si: 0.4 to 2%, Cu: 0.8 to 1.4%, Mg + Cu: 0.9 to 1.5% by weight% Zn: 0.03 to 1.5%, Mn: 0.03 to 0.2%, Cr: 0.03 to 0.2%, Zr: 0.03 to 0.15%, V: 0.03 to 0.15%, Fe: 0.03 to 0.3%, Ti: 0.005 to 0.1%, one or more of which are further contained, with the balance being Al and inevitable Alloy containing chemical impurities, and the maximum diameter of a precipitate containing Cu on a crystal grain boundary is 0.5 μm
And less than 5% of the crystal grain interface, and the number of crystal precipitates having a maximum diameter of 0.2 μm or more in the grains is less than 20 per 100 μm 2. Al-Mg with excellent corrosion resistance and moldability
-Si-Cu alloy plate.
ｕ系合金板の製造方法であって、冷間圧延後の溶体化処
理を５２０℃以上で５分以下とし、溶体化処理後の冷却
を溶体化温度〜２００℃の温度域の冷却速度を１５℃／
ｓｅｃ超とすることを特徴とする耐食性および成形性に
優れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板の製造方法。2. The Al-Mg-Si-C according to claim 1,
A method for producing a u-based alloy sheet, wherein the solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and the cooling after the solution treatment is performed at a cooling rate of 15 ° C. to 200 ° C. ° C /
A method for producing an Al-Mg-Si-Cu-based alloy sheet having excellent corrosion resistance and formability, characterized in that the time is longer than sec.
ｕ系合金板の製造方法であって、熱間圧延後に２５０℃
以上４５０℃未満で０．５〜４時間の保持を施すことを
特徴とするＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板の製造方
法。3. The Al-Mg-Si-C according to claim 1,
A method for producing a u-based alloy sheet, comprising:
A method for producing an Al-Mg-Si-Cu-based alloy sheet, wherein the holding is performed at a temperature lower than 450 ° C for 0.5 to 4 hours.
ｕ系合金板の製造方法であって、冷間圧延後の溶体化処
理を５２０℃以上で５分以下とし、溶体化処理後の冷却
を溶体化温度〜２００℃の温度域の冷却速度を１５℃／
ｓｅｃ超とし、４０〜１００℃で巻取った後、０．１〜
１０℃／ｈの冷却速度で冷却することを特徴とする耐食
性および成形性に優れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金
板の製造方法。4. The Al-Mg-Si-C according to claim 1,
A method for producing a u-based alloy sheet, wherein the solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and the cooling after the solution treatment is performed at a cooling rate of 15 ° C. to 200 ° C. ° C /
sec, and after winding at 40-100 ° C, 0.1-
A method for producing an Al-Mg-Si-Cu alloy sheet having excellent corrosion resistance and formability, characterized by cooling at a cooling rate of 10 ° C / h.
ｕ系合金板の製造方法であって、冷間圧延後の溶体化処
理を５２０℃以上で５分以下とし、溶体化処理後の冷却
を溶体化温度〜２００℃の温度域の冷却速度を１５℃／
ｓｅｃ超とし、４０〜１００℃で巻取った後、４０〜１
００℃で０．５〜５０時間保持することを特徴とする耐
食性および成形性に優れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合
金板の製造方法。5. The Al-Mg-Si-C according to claim 1,
A method for producing a u-based alloy sheet, wherein the solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and the cooling after the solution treatment is performed at a cooling rate of 15 ° C. to 200 ° C. ° C /
sec, and after winding at 40-100 ° C, 40-1
A method for producing an Al-Mg-Si-Cu-based alloy sheet having excellent corrosion resistance and formability, which is maintained at 00C for 0.5 to 50 hours.
ｕ系合金板の製造方法であって、冷間圧延後の溶体化処
理を５２０℃以上で５分以下とし、溶体化処理後の冷却
を溶体化温度〜２００℃の温度域の冷却速度を１５℃／
ｓｅｃ超とし、４０〜１００℃で巻取った後、０．１〜
１０℃／ｈの冷却速度で冷却し、さらに１３０〜２８０
℃に加熱して０超〜３０分保持することを特徴とする耐
食性および成形性に優れたＡｌ−Ｍｇ−Ｓｉ−Ｃｕ系合
金板の製造方法。6. The Al-Mg-Si-C according to claim 1,
A method for producing a u-based alloy sheet, wherein the solution treatment after cold rolling is performed at 520 ° C. or more and 5 minutes or less, and the cooling after the solution treatment is performed at a cooling rate of 15 ° C. to 200 ° C. ° C /
sec, and after winding at 40-100 ° C, 0.1-
Cool at a cooling rate of 10 ° C./h,
A method for producing an Al-Mg-Si-Cu alloy sheet excellent in corrosion resistance and formability, characterized in that the sheet is heated to 0C and held for more than 0 to 30 minutes.
ｕ系合金板を製造方法であって、冷間圧延後の溶体化処
理を５２０℃以上で５分以下とし、溶体化処理後の冷却
を溶体化温度〜２００℃の温度域の冷却速度を１５℃／
ｓｅｃ超とし、４０〜１００℃で巻取った後、０．１〜
１０℃／ｈの冷却速度で冷却し、さらに１３０〜２８０
℃に加熱して０超〜３０分保時した後、４０〜１００℃
まで冷却して巻取り、０．１〜１０℃／ｈの冷却速度で
冷却することを特徴とする耐食性および成形性に優れた
Ａｌ−Ｍｇ−Ｓｉ−Ｃｕ系合金板の製造方法。7. The Al-Mg-Si-C according to claim 1,
A method for producing a u-based alloy sheet, wherein the solution treatment after cold rolling is performed at a temperature of 520 ° C. or more and 5 minutes or less, and the cooling after the solution treatment is performed at a cooling rate of 15 ° C. to 200 ° C. ° C /
sec, and after winding at 40-100 ° C, 0.1-
Cool at a cooling rate of 10 ° C./h,
After heating to 0 ° C and keeping for more than 0 to 30 minutes, 40 to 100 ° C
A method for producing an Al-Mg-Si-Cu alloy sheet excellent in corrosion resistance and formability, wherein the sheet is cooled and wound up, and cooled at a cooling rate of 0.1 to 10 ° C / h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000034464A JP2001020027A (en) | 1999-05-06 | 2000-02-14 | Al-Mg-Si-Cu ALLOY SHEET EXCELLENT IN CORROSION RESISTANCE AND FORMABILITY, AND ITS MANUFACTURE |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12541399 | 1999-05-06 | ||
| JP11-125413 | 1999-05-06 | ||
| JP2000034464A JP2001020027A (en) | 1999-05-06 | 2000-02-14 | Al-Mg-Si-Cu ALLOY SHEET EXCELLENT IN CORROSION RESISTANCE AND FORMABILITY, AND ITS MANUFACTURE |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2001020027A true JP2001020027A (en) | 2001-01-23 |
Family
ID=26461859
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2000034464A Withdrawn JP2001020027A (en) | 1999-05-06 | 2000-02-14 | Al-Mg-Si-Cu ALLOY SHEET EXCELLENT IN CORROSION RESISTANCE AND FORMABILITY, AND ITS MANUFACTURE |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2001020027A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001295008A (en) * | 2000-04-13 | 2001-10-26 | Nissan Motor Co Ltd | Aluminum alloy sheet excellent in filiform erosion resistance and its producing method |
| JP2003105471A (en) * | 2001-09-28 | 2003-04-09 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet, and production method therefor |
| JP2003105472A (en) * | 2001-09-28 | 2003-04-09 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet, and production method therefor |
| JP2004124175A (en) * | 2002-10-02 | 2004-04-22 | Furukawa Sky Kk | Method for manufacturing 6000 system alloy plate for forming excellent in formability, baking hardenability, and springback characteristic |
| JP2008297630A (en) * | 2001-05-03 | 2008-12-11 | Novelis Inc | Process for making aluminum alloy having excellent bendability |
| JP2013185218A (en) * | 2012-03-08 | 2013-09-19 | Kobe Steel Ltd | Aluminum alloy sheet excellent in baking finish hardenability |
| KR101950595B1 (en) * | 2017-08-22 | 2019-02-20 | 현대제철 주식회사 | Aluminium alloy and methods of fabricating the same |
| WO2019089736A1 (en) | 2017-10-31 | 2019-05-09 | Arconic Inc. | Improved aluminum alloys, and methods for producing the same |
-
2000
- 2000-02-14 JP JP2000034464A patent/JP2001020027A/en not_active Withdrawn
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001295008A (en) * | 2000-04-13 | 2001-10-26 | Nissan Motor Co Ltd | Aluminum alloy sheet excellent in filiform erosion resistance and its producing method |
| JP2008297630A (en) * | 2001-05-03 | 2008-12-11 | Novelis Inc | Process for making aluminum alloy having excellent bendability |
| JP2003105471A (en) * | 2001-09-28 | 2003-04-09 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet, and production method therefor |
| JP2003105472A (en) * | 2001-09-28 | 2003-04-09 | Sumitomo Light Metal Ind Ltd | Aluminum alloy sheet, and production method therefor |
| JP2004124175A (en) * | 2002-10-02 | 2004-04-22 | Furukawa Sky Kk | Method for manufacturing 6000 system alloy plate for forming excellent in formability, baking hardenability, and springback characteristic |
| JP2013185218A (en) * | 2012-03-08 | 2013-09-19 | Kobe Steel Ltd | Aluminum alloy sheet excellent in baking finish hardenability |
| KR101950595B1 (en) * | 2017-08-22 | 2019-02-20 | 현대제철 주식회사 | Aluminium alloy and methods of fabricating the same |
| WO2019089736A1 (en) | 2017-10-31 | 2019-05-09 | Arconic Inc. | Improved aluminum alloys, and methods for producing the same |
| EP3704279A4 (en) * | 2017-10-31 | 2021-03-10 | Howmet Aerospace Inc. | Improved aluminum alloys, and methods for producing the same |
| US11608551B2 (en) | 2017-10-31 | 2023-03-21 | Howmet Aerospace Inc. | Aluminum alloys, and methods for producing the same |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5371173B2 (en) | Manufacturing method of high strength aluminum alloy fin material | |
| JP4901757B2 (en) | Aluminum alloy plate and manufacturing method thereof | |
| JP4725019B2 (en) | Aluminum alloy fin material for heat exchanger, manufacturing method thereof, and heat exchanger provided with aluminum alloy fin material | |
| WO2009122869A1 (en) | Cu-Ni-Si-Co COPPER ALLOY FOR ELECTRONIC MATERIAL AND PROCESS FOR PRODUCING THE SAME | |
| JP6022882B2 (en) | High strength aluminum alloy extruded material and manufacturing method thereof | |
| WO2011036804A1 (en) | Cu-Ni-Si-Co COPPER ALLOY FOR ELECTRONIC MATERIAL AND PROCESS FOR PRODUCING SAME | |
| JP5113318B2 (en) | Aluminum alloy plate for forming and method for producing the same | |
| JP2008024964A (en) | High-strength aluminum alloy sheet and producing method therefor | |
| EP0480402B1 (en) | Process for manufacturing aluminium alloy material with excellent formability, shape fixability and bake hardenability | |
| JP4634249B2 (en) | Aluminum alloy plate for forming and method for producing the same | |
| JP5195837B2 (en) | Aluminum alloy fin material for heat exchanger | |
| JPH11310841A (en) | Aluminum alloy extruded shape excellent in fatigue strength, and its production | |
| JPH0931616A (en) | Aluminum-magnesium-silicon alloy sheet excellent in formability and its production | |
| JP2008025006A (en) | Aluminum alloy sheet having excellent stress corrosion cracking resistance | |
| JP3849095B2 (en) | Aluminum alloy plate for forming and method for producing the same | |
| JP3845312B2 (en) | Aluminum alloy plate for forming and method for producing the same | |
| JP2001020027A (en) | Al-Mg-Si-Cu ALLOY SHEET EXCELLENT IN CORROSION RESISTANCE AND FORMABILITY, AND ITS MANUFACTURE | |
| JP3734317B2 (en) | Method for producing Al-Mg-Si alloy plate | |
| JP2003239052A (en) | Method for producing aluminum foil base material and method for producing aluminum foil | |
| JP2004027253A (en) | Aluminum alloy sheet for molding, and method of producing the same | |
| JP6581347B2 (en) | Method for producing aluminum alloy plate | |
| JP2008231475A (en) | Aluminum alloy sheet for forming workpiece, and producing method therefor | |
| JP5166702B2 (en) | 6000 series aluminum extrudate excellent in paint bake hardenability and method for producing the same | |
| JP2001032031A (en) | Aluminum alloy sheet for structural material, excellent in stress corrosion cracking resistance | |
| JP2005139530A (en) | Method of producing aluminum alloy sheet for forming |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20070501 |