JP2000096175A - Aluminum alloy sheet excellent in ridging mark resistance - Google Patents

Aluminum alloy sheet excellent in ridging mark resistance

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Publication number
JP2000096175A
JP2000096175A JP27009398A JP27009398A JP2000096175A JP 2000096175 A JP2000096175 A JP 2000096175A JP 27009398 A JP27009398 A JP 27009398A JP 27009398 A JP27009398 A JP 27009398A JP 2000096175 A JP2000096175 A JP 2000096175A
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JP
Japan
Prior art keywords
aluminum alloy
alloy sheet
less
sheet
ridging
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
JP27009398A
Other languages
Japanese (ja)
Other versions
JP3498942B2 (en
Inventor
Takehiko Eto
Manabu Nakai
学 中井
武比古 江藤
Original Assignee
Kobe Steel Ltd
株式会社神戸製鋼所
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Application filed by Kobe Steel Ltd, 株式会社神戸製鋼所 filed Critical Kobe Steel Ltd
Priority to JP27009398A priority Critical patent/JP3498942B2/en
Publication of JP2000096175A publication Critical patent/JP2000096175A/en
Application granted granted Critical
Publication of JP3498942B2 publication Critical patent/JP3498942B2/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Abstract

PROBLEM TO BE SOLVED: To obtain an aluminum alloy free from the occurrence of ridging mark. SOLUTION: The aluminum alloy sheet is an Al-Mg-Si type aluminum alloy sheet which has a composition containing, by mass, 0.2-1.8% Si and 0.2-1.6% Mg and is prepared by carring out hot rolling, successive cold rolling after process annealing if necessary, solution heat treatment, and hardening treatment. Moreover, the alloy sheet has a microstructure composed of equiaxed recrystallized grains. Further, the rate of earing of a cup becomes >=-4% when the alloy sheet is subjected to forming into a cup shape at 150 kgf blank holder pressure and 60 mm/min forming rate by the use of #700 lubricating oil by using a 40 mm diameter punch (3 mm shoulder radius) and a die in which the ratio of the clearance between punch and die to the thickness of the Al alloy sheet is 1.3-1.4. It is desirable that this Al alloy sheet has <=45 μm grain size.

Description

【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION
【0001】[0001]
【発明の属する技術分野】本発明は、耐リジングマーク
性に優れ、自動車、鉄道車両及び航空機等の輸送機用パ
ネルとしての用途に適するAl−Mg−Si系アルミニ
ウム合金板に関する。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an Al-Mg-Si-based aluminum alloy plate which has excellent ridging mark resistance and is suitable for use as a panel for a transport device such as an automobile, a railway vehicle and an aircraft.
【0002】[0002]
【従来の技術】6000系(Al−Mg−Si系)アル
ミニウム合金板材は、耐食性及び常温での成形加工性が
比較的優れ、人工時効処理により高強度が得られること
から、成形性あるいは軽量化、薄肉化が要求される用途
に適している。Al−Mg−Si系合金板材は、通常、
均質化処理後、熱間圧延し、続いて必要に応じて中間焼
鈍した後、冷間圧延を施して所定厚の板材とし、これに
溶体化及び焼入れ処理を施し、さらにその後必要に応じ
てスキンパス、ストレッチ等を施して製造される。
2. Description of the Related Art A 6000 (Al-Mg-Si) aluminum alloy sheet is relatively excellent in corrosion resistance and formability at room temperature, and has high strength by artificial aging. It is suitable for applications requiring thinning. Al-Mg-Si based alloy sheet materials are usually
After the homogenization treatment, hot rolling is performed, and then, if necessary, intermediate annealing is performed, and then cold rolling is performed to obtain a plate having a predetermined thickness, which is subjected to a solution treatment and a quenching treatment. , Stretched, etc.
【0003】ところが、Al−Mg−Si系合金板材に
対し成形加工を行ったとき、特開平7−228956号
公報又は特開平8−232052号公報に記載されてい
るように、板表面にリジングマークと呼ばれる表面荒れ
が発生することが問題となっている。このリジングマー
クが発生すると、表面が極めて美麗であることが要求さ
れる自動車用外板パネル、さらには旅客機胴体外板パネ
ル等の用途には外観不良として使用できず、また、リジ
ングマークは塗装を行った場合特に目立つようになるた
め、成形加工後気付かれないまま塗装工程に進み、塗装
後に初めて認識されることもある。つまり製品になって
初めて現れることがあるという困った特性を持ってい
る。
However, when a forming process is performed on an Al-Mg-Si alloy sheet material, a ridging mark is formed on the surface of the sheet as described in JP-A-7-228956 or JP-A-8-23252. The problem is that surface roughness called "surface roughness" occurs. When this ridging mark occurs, it cannot be used as a poor appearance for applications such as automotive skin panels that require a very beautiful surface, and passenger aircraft fuselage skin panels, and ridging marks must be painted. If it is performed, it becomes particularly noticeable, so it proceeds to the painting process without noticing after the molding process, and it may be recognized for the first time after painting. In other words, it has the troublesome characteristic that it sometimes appears only when it is a product.
【0004】前記特開平7−228956号公報及び特
開平8−232052号公報は、Al−Mg−Si系合
金板材についてリジングマークの発生を防止する方法に
関し、前者が、均質化処理後350〜450℃の温度ま
で冷却して熱間圧延を開始し、200〜300℃の温度
で熱間圧延を終了し、必要に応じて中間焼鈍を行った
後、冷間圧延、溶体化及び焼入れ処理を施すというも
の、後者が、均質化処理後450℃以下の温度まで冷却
して熱間圧延を開始し、200〜350℃の温度で熱間
圧延を終了し、必要に応じて350〜420℃の中間焼
鈍を行った後、冷間圧延、溶体化焼入れ、さらに最終加
熱処理を施すというものであり、いずれも熱間圧延温度
を低めに設定し、同時にその他の各工程の処理条件も厳
密に制御し、それによってリジングマークの発生を防止
しようというものである。
Japanese Patent Application Laid-Open Nos. Hei 7-228956 and Hei 8-23205 relate to a method for preventing the generation of ridging marks on an Al-Mg-Si alloy sheet material. Cooling to a temperature of 200 ° C. starts hot rolling, ends hot rolling at a temperature of 200 to 300 ° C., performs intermediate annealing as necessary, and then performs cold rolling, solution treatment, and quenching. That is, the latter is cooled to a temperature of 450 ° C. or less after the homogenization treatment, and starts hot rolling, finishes hot rolling at a temperature of 200 to 350 ° C., and intermediates the temperature of 350 to 420 ° C. as necessary. After annealing, cold rolling, solution quenching, and final heat treatment are performed.In each case, the hot rolling temperature is set lower, and at the same time, the processing conditions in each of the other steps are strictly controlled. It depends It is that you try to prevent the occurrence of ridging marks Te.
【0005】[0005]
【発明が解決しようとする課題】一方、本発明者らは、
先に特願平9−287906号、特願平9−36772
3号において、Si:0.2〜1.8%、Mg:0.2
〜1.6%を含有する成形加工用Al−Mg−Si系ア
ルミニウム合金板のマクロ組織のサイズ又はキューブ方
位の集積度を所定の範囲に規制することにより、リジン
グマークの発生を防止できることを見いだした。しかし
ながら、マクロ組織の形態又はキューブ方位の集積度を
統計処理し、それより製品全体(例えばコイル全長)の
特性のバラツキを推定することは時間的にもコスト的に
も実製造ラインにおいては、現実的ではない。
On the other hand, the present inventors have
First, Japanese Patent Application Nos. 9-287906 and 9-36772.
In No. 3, Si: 0.2 to 1.8%, Mg: 0.2
It has been found that the occurrence of ridging marks can be prevented by regulating the size of the macrostructure or the degree of integration of the cube orientation of the Al-Mg-Si-based aluminum alloy sheet for forming containing up to 1.6% to a predetermined range. Was. However, to statistically process the form of the macrostructure or the degree of integration of the cube orientation and to estimate the variation in the characteristics of the entire product (for example, the entire length of the coil) based on the statistical processing, in an actual manufacturing line in terms of time and cost, it is not practical. Not a target.
【0006】その点、もしアルミニウム合金板における
多数のサンプルの特性を短時間で測定することで、高い
信頼度で評価できれば、例えばリジングマークが発生し
やすい製品板と判定された場合には、工場からの出荷を
停止することができる。また、そのような製品板は、成
形加工時に大きな引張変形を受けない部材に転用して出
荷することも可能となり、品質及び歩留りの向上を図る
ことができる。そして、先願のマクロ組織のサイズ又は
キューブ方位の集積度の規定は、リジングマークの発生
を防止するための必要条件ではあるが、上記の規定を満
たしているものでも、成形加工及び電着塗装後まれにリ
ジングマークが発見される場合があり、必ずしも十分条
件ではない可能性があった。従って、リジングマークの
発生の有無を評価できるさらに確実性の高い指標が望ま
れている。すなわち、本発明は、アルミニウム合金板に
おいてリジングマークが発生するかどうかを、短時間
で、確実に評価できるようにすることを目的とする。
In this regard, if the characteristics of a large number of samples of an aluminum alloy plate can be measured in a short time and evaluated with high reliability, for example, if it is determined that the product plate is prone to produce ridging marks, it will not be used in a factory. Can be stopped. In addition, such a product plate can be diverted to a member that is not subjected to a large tensile deformation at the time of molding and can be shipped, and the quality and the yield can be improved. The definition of the macrostructure size or the degree of integration of the cube orientation in the prior application is a necessary condition for preventing the occurrence of ridging marks. Ridging marks may be discovered in rare cases, which may not always be sufficient. Therefore, a more reliable index that can evaluate the presence or absence of a ridging mark is desired. That is, an object of the present invention is to make it possible to reliably and quickly evaluate whether or not ridging marks are generated in an aluminum alloy plate.
【0007】[0007]
【課題を解決するための手段】本発明者らは、Al−M
g−Si系アルミニウム合金を特定の温度及び歪速度条
件下で熱間圧延し、かつ熱間圧延後のミクロ組織を等軸
状再結晶粒としておけば、中間焼鈍を行い又は行うこと
なく、必要に応じて冷間圧延を行い、その後溶体化処理
及び焼入れを行い、ミクロ組織が等軸状再結晶粒である
製品板としたとき、製品板にリジングマークが発生する
のを防止できることを見いだし、先に特許出願した。な
お、この等軸状再結晶粒とは、板面に平行な面及び圧延
方向に垂直な面の両方において、観察される再結晶粒の
平均アスペクト比が1〜3の範囲内にあることを意味す
る。具体的にいえば、次の条件を満たす。 1≦dL/dLT≦3 1≦dL/dST≦3 dL ;板の長さ方向に測定した粒径 dLT;板の幅方向に測定した粒径 dST;板厚方向に測定した粒径
Means for Solving the Problems The present inventors have proposed Al-M
If the g-Si based aluminum alloy is hot-rolled under specific temperature and strain rate conditions, and the microstructure after hot rolling is set as equiaxed recrystallized grains, it is necessary to perform intermediate annealing or not. Cold rolling is performed in accordance with, then solution treatment and quenching are performed, and when the microstructure is a product plate with equiaxed recrystallized grains, it is found that ridging marks can be prevented from being generated on the product plate, I applied for a patent earlier. In addition, this equiaxed recrystallized grain means that the average aspect ratio of the recrystallized grain observed in both the plane parallel to the plate surface and the plane perpendicular to the rolling direction is in the range of 1 to 3. means. Specifically, the following condition is satisfied. 1 ≦ dL / dLT ≦ 3 1 ≦ dL / dST ≦ 3 dL; particle size measured in the plate length direction dLT; particle size measured in the plate width direction dST; particle size measured in the plate thickness direction
【0008】その後、熱延及び続いて必要に応じて中間
焼鈍を行った後冷延し、その後溶体化及び焼入れ処理し
ミクロ組織を等軸状再結晶粒としたAl−Mg−Si系
アルミニウム合金製品板について、その特性を種々検討
した結果、リジングマークの発生の有無とこの製品板を
カップ状に成形加工したとき発生する耳高さの間に、あ
る特定の関係があることが見いだされた。本発明はこの
知見に基づいてなされたもので、Si:0.2〜1.8
%、Mg:0.2〜1.6%を含有し、熱延及び続いて
必要に応じて中間焼鈍した後冷延し、その後溶体化及び
焼入れ処理されたAl−Mg−Si系アルミニウム合金
板であり、ミクロ組織が等軸状の再結晶粒からなり、さ
らに「直径40mmのポンチ(肩部半径3mm)及びポ
ンチとダイスの隙間とAl合金板厚の比が1.3〜1.
4の範囲のダイスを用い、しわ押え力150kgf、成
形速度60mm/分、使用潤滑油#700」の条件でカ
ップ状に成形加工したとき、カップ耳率が−4%以上で
あることを特徴とする。なお、等軸状の意味は先に示し
たものと同じである。
[0008] Thereafter, Al-Mg-Si-based aluminum alloys are subjected to hot rolling and, if necessary, intermediate annealing, and then cold rolled, and then subjected to a solution treatment and a quenching treatment to make the microstructure equiaxed recrystallized grains. As a result of various studies on the characteristics of the product plate, it was found that there was a specific relationship between the presence or absence of ridging marks and the ear height generated when this product plate was formed into a cup shape. . The present invention has been made based on this finding, and Si: 0.2 to 1.8.
%, Mg: 0.2 to 1.6%, an Al-Mg-Si-based aluminum alloy plate that has been hot-rolled and subsequently subjected to intermediate annealing if necessary, then cold-rolled, and then solution-hardened and quenched. The microstructure is composed of equiaxed recrystallized grains, and the ratio of the Al alloy sheet thickness to the punch having a diameter of 40 mm (shoulder radius of 3 mm) and the gap between the punch and the die is 1.3 to 1.
When a die in the range of 4 is used to form a cup under the conditions of a wrinkle holding force of 150 kgf, a forming speed of 60 mm / min, and a used lubricating oil # 700, the cup ear ratio is -4% or more. I do. The equiaxed meaning is the same as that described above.
【0009】[0009]
【発明の実施の形態】Al−Mg−Si系アルミニウム
合金板をカップ状に成形加工したとき発生する耳は、マ
イナス耳と称される圧延方向に対し0゜、90゜、18
0゜、270゜方向に発生する耳と、プラス耳と称され
る圧延方向に対し45゜、135゜、225゜、315
゜方向に発生する耳に大別される。そして、耳率(%)
は下記の通り一般に定義される。 耳率(%)={(プラス耳の高さの平均値)−(マイナ
ス耳の高さの平均値)}×100/(平均耳高さ)
DESCRIPTION OF THE PREFERRED EMBODIMENTS Ears generated when an Al-Mg-Si based aluminum alloy plate is formed into a cup shape are 0 °, 90 °, 18 ° with respect to a rolling direction called a minus ear.
0 °, 270 ° ears and 45 °, 135 °, 225 °, 315
It is roughly divided into ears that occur in the ゜ direction. And ear rate (%)
Is generally defined as follows: Ear ratio (%) = {(average value of plus ear height) − (average value of minus ear height)} × 100 / (average ear height)
【0010】先の出願に示したように、熱延及び続いて
必要に応じて中間焼鈍を行った後冷延し、その後溶体化
及び焼入れ処理されたAl−Mg−Si系アルミニウム
合金板におけるリジングマーク発生の有無はキューブ方
位の集積度に関係している。キューブ方位の集積度が高
いと、成形時にキューブ方位の集積領域と非集積領域で
変形の異方性及び変形程度に差が生じ、これがリジング
マークの発生の原因となるのであるから、成形加工時に
起こる変形の異方性をより直接的に表わす耳率を用いる
ことにより、リジングマーク発生の有無をより正確に評
価できるようなる可能性がある。その観点から、本発明
者らが熱延及び続いて中間焼鈍を行った後冷延し、その
後溶体化及び焼入れ処理しミクロ組織を等軸状再結晶粒
としたAl−Mg−Si系アルミニウム合金板につい
て、一定の加工条件(前記「」内)でカップ状に成形加
工して検討したところ、上記に定義された耳率が−4%
以上の板において、リジングマークの発生が確実に防止
されることが分かった。なお、カップ状に成形加工した
ときの耳率は加工条件により変動するので、加工条件は
一定でなくてはならない。
[0010] As shown in the prior application, ridging in an Al-Mg-Si-based aluminum alloy plate which has been hot-rolled, and subsequently subjected to intermediate annealing as required, then cold-rolled, and then solution-hardened and quenched. The presence or absence of the mark is related to the degree of integration of the cube orientation. If the degree of integration of the cube orientation is high, there is a difference in the anisotropy and degree of deformation between the accumulation area and the non-accumulation area of the cube orientation during molding, which causes the generation of ridging marks. The use of ear ratios that more directly represent the anisotropy of the resulting deformation may allow more accurate assessment of the presence or absence of ridging marks. From that point of view, the present inventors performed hot rolling and subsequently intermediate annealing, then cold rolled, and then subjected to solution treatment and quenching treatment to make the microstructure an equiaxed recrystallized Al-Mg-Si based aluminum alloy. When the plate was formed into a cup shape under a certain processing condition (in the above "") and examined, the ear ratio defined above was -4%.
It was found that in the above plate, the occurrence of ridging marks was reliably prevented. In addition, since the ear ratio at the time of forming into a cup shape varies depending on the processing conditions, the processing conditions must be constant.
【0011】熱延及び続いて必要に応じて中間焼鈍を行
った後冷延後、溶体化及び焼入れ処理しミクロ組織を等
軸状再結晶粒としたAl−Mg−Si系アルミニウム合
金板を上記の条件でカップ状に成形加工し、そのときの
耳率が上記の範囲内のとき、製品板の耐リジングマーク
性が保証される。しかし、耳率が上記の範囲外のとき、
耐リジングマーク性は完全には保証されない。従って、
この場合は、製品板をリジングマークが発生しないレベ
ルの成形加工用途又はリジングマークが発生しても構わ
ない用途に回すなどの対処を行う。いずれにしても耳高
さの測定は簡便で短時間に行えるので、迅速な対処が可
能である。なお、カップ状に成形加工する条件について
は、必ずしも前記「」と同一である必要はない。しか
し、その条件で成形加工したときの耳率とリジングマー
ク発生の関係が明らかにされている必要がある。
[0011] The Al-Mg-Si-based aluminum alloy sheet having a microstructure of equiaxed recrystallized grains by hot rolling, and then, if necessary, intermediate annealing and then cold rolling, solution treatment and quenching, is used. When the ear ratio at that time is within the above range, the ridging mark resistance of the product plate is guaranteed. However, when the ear rate is outside the above range,
Ridging mark resistance is not completely guaranteed. Therefore,
In this case, a countermeasure such as turning the product plate to a molding use at a level at which ridging marks are not generated or a use at which ridging marks may be generated is taken. In any case, since the measurement of the ear height can be performed easily and in a short time, quick measures can be taken. The conditions for forming into a cup shape do not necessarily have to be the same as the above-mentioned "". However, it is necessary to clarify the relationship between the ear ratio and the occurrence of ridging marks when molding is performed under these conditions.
【0012】上記Al−Mg−Si系アルミニウム合金
板は、均質化熱処理後熱間圧延し、必要に応じて中間焼
鈍を行い、続いて冷間圧延、溶体化処理及び焼入れが行
われるが、それぞれの好ましい条件は以下の通りであ
る。熱間圧延は、熱間圧延終了温度を再結晶温度以上と
し、かつ熱間圧延の最終パス時の歪速度を7000〜2
0000%/secとし、熱延終了後直ちに巻き上げて
ミクロ組織が等軸状の再結晶粒となった熱延板を得る。
ここで、歪速度は、 歪速度=最終ロールによる圧延率(%)÷最終ロールを
板が通過する時間(秒) で定義される。より具体的には、圧延開始温度を450
℃以上、均質化処理温度(例えば470〜540℃)以
下とし、熱間圧延終了温度を再結晶温度以上、例えば3
00〜450℃と設定する。仕上げ熱間圧延を複数段の
連続式で行う場合、連続した熱間圧延の最低歪速度を最
終パス時歪み速度の2%以上とし、仕上げ熱間圧延の
間、再結晶が繰り返し起こるようにすれば、再結晶粒が
微細化し、かつ製品板のリジングマーク防止に一層効果
的である。この段階での再結晶粒の好ましい粒径は45
μm以下である。さらに、仕上げ熱間圧延で再結晶を起
こさせるために、各パスの圧延率を40%以上とするこ
とが望ましい。
The Al-Mg-Si-based aluminum alloy sheet is subjected to hot rolling after homogenizing heat treatment, intermediate annealing as necessary, followed by cold rolling, solution treatment and quenching. Are as follows. In the hot rolling, the hot rolling end temperature is equal to or higher than the recrystallization temperature, and the strain rate during the final pass of the hot rolling is 7000 to 2
After the completion of hot rolling, the rolled sheet is immediately rolled up to obtain a hot-rolled sheet having microstructure of equiaxed recrystallized grains.
Here, the strain rate is defined as: strain rate = rolling rate (%) by final roll / time (second) that the sheet passes through the final roll. More specifically, the rolling start temperature is set to 450
° C or higher and a homogenization treatment temperature (for example, 470 to 540 ° C) or lower, and the hot rolling end temperature is higher than the recrystallization temperature, for example, 3 ° C.
Set to 00-450 ° C. In the case where the finishing hot rolling is performed in a continuous manner in a plurality of stages, the minimum strain rate of the continuous hot rolling is set to 2% or more of the strain rate at the time of the final pass, and recrystallization is repeatedly performed during the finishing hot rolling. If this is the case, the recrystallized grains become finer, and this is more effective in preventing ridging marks on the product plate. The preferred size of the recrystallized grains at this stage is 45
μm or less. Further, in order to cause recrystallization in the finish hot rolling, it is desirable that the rolling ratio of each pass is 40% or more.
【0013】中間焼鈍条件は、加熱速度:400℃まで
を30℃/分〜500℃/秒、400〜500℃を10
〜100℃/分、保持条件:500〜580℃×10秒
〜10分、冷却速度:保持温度から50℃までを30℃
/分以上とする。なお、中間焼鈍を行う場合は、熱間圧
延の圧延終了温度を先の熱間圧延において記載した温度
範囲より、例えば150〜300℃と低くすることがで
きる。また、熱間圧延の最終パス時の歪み速度を例えば
5000〜20000%/秒と低く設定することができ
る。冷間圧延率は、溶体化処理後のアルミニウム合金板
の等軸状再結晶粒の粒径を45μm以下に微細化するた
め、好ましくは冷間圧延率は50%以上とする。これに
より、成形時のオレンジピールの発生が防止される。な
お、上記の中間焼鈍を行った場合は、固溶度が高く冷間
圧延での加工硬化度が高くなり、溶体化処理での再結晶
粒は微細化されやすい。従って、冷延率は30%以上で
十分である。好ましい溶体化処理条件は、400℃まで
の加熱速度は30℃/分以上、400〜530℃を10
℃/分以上、530〜580℃で10秒〜10分であ
る。加熱には、加熱速度を大きくするため、硝石炉、連
続焼鈍炉、誘導加熱炉等を用いてもよい。焼入れは、保
持温度から70〜140℃の温度又はそれ以下まで30
℃/分以上の冷却速度で行うか、保持温度から70〜1
40℃の温度に30℃/分以上の冷却速度で行い、その
まま70〜140℃の温度で0.5〜48時間の間保持
してもよい。
The intermediate annealing conditions are as follows: heating rate: up to 400 ° C., 30 ° C./min. To 500 ° C./sec.
100100 ° C./min, holding condition: 500-580 ° C. × 10 seconds to 10 minutes, cooling rate: 30 ° C. from holding temperature to 50 ° C.
/ Min or more. In the case where the intermediate annealing is performed, the rolling end temperature of the hot rolling can be made lower than the temperature range described in the previous hot rolling, for example, to 150 to 300 ° C. Further, the strain rate during the final pass of hot rolling can be set as low as, for example, 5,000 to 20,000% / sec. The cold rolling rate is preferably set to 50% or more in order to reduce the particle diameter of equiaxed recrystallized grains of the aluminum alloy sheet after solution treatment to 45 μm or less. Thereby, the occurrence of orange peel during molding is prevented. When the above-described intermediate annealing is performed, the solid solubility is high, the work hardening degree in cold rolling is high, and the recrystallized grains in the solution treatment are easily refined. Therefore, a cold rolling reduction of 30% or more is sufficient. Preferred solution treatment conditions are as follows: heating rate up to 400 ° C. is 30 ° C./min or more;
C./min or more, at 530-580.degree. C. for 10 seconds to 10 minutes. For heating, a nitrite furnace, a continuous annealing furnace, an induction heating furnace, or the like may be used to increase the heating rate. The quenching is performed from the holding temperature to a temperature of 70 to 140 ° C. or lower.
C./min. Or at a holding temperature of 70 to 1
The cooling may be performed at a temperature of 40 ° C. at a cooling rate of 30 ° C./min or more, and may be maintained at a temperature of 70 to 140 ° C. for 0.5 to 48 hours.
【0014】成分組成の面でいえば、本発明は、Si:
0.2〜1.8%、Mg:0.2〜1.6%を含有し、
残部Alと不可避不純物からなるアルミニウム合金のほ
か、必要に応じて、さらにZn:0.005〜1.0
%、Cu:0.005〜1.0%、Ti:0.001〜
0.1%のいずれか1種又は2種以上、B:1〜30
0ppm、Be:0.1〜100ppmの1種又は2
種、Mn:1.0%以下、Cr:0.3%以下、Z
r:0.15%以下、V:0.15%以下のうちから1
種又は2種以上を合計で0.01〜1.5%、以上〜
のいずれか又はこれらを組み合わせて含有するアルミ
ニウム合金など、Si:0.2〜1.8%、Mg:0.
2〜1.6%を含有するAl−Mg−Si系アルミニウ
ム合金全てに適用し得る。Al−Mg−Si系合金の組
成を上記のように規定した理由は下記のとおりである。
[0014] In terms of the component composition, the present invention relates to Si:
0.2-1.8%, Mg: 0.2-1.6%,
In addition to the aluminum alloy comprising the balance of Al and inevitable impurities, if necessary, Zn: 0.005 to 1.0
%, Cu: 0.005 to 1.0%, Ti: 0.001 to
0.1% of one or more of B, 1 to 30
0 ppm, Be: one or more of 0.1 to 100 ppm
Seed, Mn: 1.0% or less, Cr: 0.3% or less, Z
r: 0.15% or less, V: 1 out of 0.15% or less
0.01 to 1.5% in total of two or more species or more,
, Or an aluminum alloy containing a combination thereof, Si: 0.2 to 1.8%, Mg: 0.
It can be applied to all Al-Mg-Si-based aluminum alloys containing 2 to 1.6%. The reason for defining the composition of the Al-Mg-Si-based alloy as described above is as follows.
【0015】Mg:MgはSiとともに強度を付与する
元素であるが、0.2%未満では人工時効で十分な強度
が得られず、一方、1.6%を越えると成形性が低下す
る。従って、Mg含有量は0.2〜1.6%の範囲とす
る。 Si:SiはMgとともに強度を付与する元素である
が、0.2%未満では人工時効で十分な強度が得られ
ず、一方、1.8%を越えると伸びが低くなり、成形性
が低下する。従って、Si含有量は0.2〜1.8%の
範囲とする。なお、人工時効で高い強度を得るには、M
gとSiとの含有量の割合を、Si/Mg≧0.65と
することが望ましい。
Mg: Mg is an element that imparts strength together with Si, but if it is less than 0.2%, sufficient strength cannot be obtained by artificial aging, while if it exceeds 1.6%, formability decreases. Therefore, the Mg content is in the range of 0.2 to 1.6%. Si: Si is an element that imparts strength together with Mg, but if it is less than 0.2%, sufficient strength cannot be obtained by artificial aging, while if it exceeds 1.8%, elongation decreases and moldability decreases. I do. Therefore, the Si content is in the range of 0.2 to 1.8%. In order to obtain high strength by artificial aging, M
It is desirable that the ratio of the content of g and Si be Si / Mg ≧ 0.65.
【0016】Zn:Znは人工時効時においてMgZn
を微細かつ高密度に析出させ高い強度を実現させる。
ただし、0.005%未満では十分な強度が得られず、
一方1.0%を越えると耐食性が顕著に低下するため、
含有量は0.005〜1.0%の範囲とする。 Cu:Cuは人工時効時にMgSiを微細にかつ高密
度に析出させ、高い強度を実現させる。ただし、0.0
05%未満では効果がなく、一方、1.0%を越えると
耐食性及び溶接性が顕著に低下するため、含有量は0.
005〜1.0%の範囲とする。 Ti:Tiは鋳塊の結晶粒を微細化し、成形性を向上さ
せるために添加する元素であるが、0.001%未満で
は効果がなく、一方、0.1%を越えて添加されると粗
大な晶出物を形成し、成形性を低下させる。このため、
Ti含有量は0.001〜0.1%の範囲とする。
Zn: Zn is MgZn during artificial aging.
2 is finely and densely deposited to realize high strength.
However, if less than 0.005%, sufficient strength cannot be obtained,
On the other hand, if it exceeds 1.0%, the corrosion resistance is significantly reduced,
The content is in the range of 0.005 to 1.0%. Cu: Cu precipitates Mg 2 Si finely and at high density during artificial aging, and realizes high strength. However, 0.0
If it is less than 0.05%, there is no effect, while if it exceeds 1.0%, the corrosion resistance and weldability are remarkably reduced.
005 to 1.0%. Ti: Ti is an element added for refining the crystal grains of the ingot and improving formability. However, if it is less than 0.001%, there is no effect, and if it is added more than 0.1%, it is not effective. It forms coarse crystals and reduces moldability. For this reason,
The Ti content is in the range of 0.001 to 0.1%.
【0017】B:BはTiと同様に鋳塊の結晶粒を微細
化し、成形性を向上させるために添加する合金である
が、1ppm未満の添加では効果がなく、300ppm
を越えて含有されると粗大な晶出物を形成し、成形性を
低下させる。このため、B含有量は1〜300ppmの
範囲とする。 Be:Beは空気中におけるアルミニウム溶湯の再酸化
を防止するため、必要があれば0.1ppm以上含有さ
せる。しかし、100ppmを越えると材料硬度が増大
し成形性が低下するため、Be含有量は0.1〜100
ppmの範囲とする。
B: Similar to Ti, B is an alloy added for refining the crystal grains of the ingot and improving the formability. However, if less than 1 ppm is added, there is no effect.
If contained in excess of the above, a coarse crystallized product is formed and the moldability is reduced. Therefore, the B content is in the range of 1 to 300 ppm. Be: Be is contained in an amount of 0.1 ppm or more, if necessary, to prevent reoxidation of the aluminum melt in the air. However, if the content exceeds 100 ppm, the hardness of the material increases and the formability decreases.
ppm range.
【0018】Mn、Cr、Zr、V:これらの成分は均
質化熱処理時及びその後の熱間圧延時にAl20Cu
Mn、Al12MgCr、AlZr、AlMg
Zn等の分散粒子を生成する。これらの分散粒子は
再結晶後の粒界移動を妨げる効果があるため、微細な結
晶粒を得ることができる。しかし、過剰な添加は溶解鋳
造時に粗大な不溶性金属間化合物を生成しやすく、成形
加工時の破壊の起点となり、成形性を低下させる原因と
なる。また、Zrの過剰添加はミクロ組織を針長状にし
やすく、特定方向の破壊靭性及び疲労特性さらには成形
性を劣化させる。このため、Mn、Cr、Zr、Vそれ
ぞれの添加量は、1.0%、0.30%、0.15%、
0.15%以下、合計では1.5%以下とする。
Mn, Cr, Zr, V: These components are Al 20 Cu 2 during the homogenizing heat treatment and during the subsequent hot rolling.
Mn 3 , Al 12 Mg 2 Cr, Al 3 Zr, Al 2 Mg
It generates dispersed particles of 3 Zn 3 and the like. Since these dispersed particles have an effect of hindering the movement of the grain boundary after recrystallization, fine crystal grains can be obtained. However, excessive addition tends to generate a coarse insoluble intermetallic compound at the time of melting casting, becomes a starting point of destruction at the time of forming, and causes a reduction in formability. In addition, excessive addition of Zr tends to make the microstructure needle-like, deteriorating fracture toughness and fatigue characteristics in a specific direction, and further deteriorating formability. Therefore, the addition amounts of Mn, Cr, Zr, and V are 1.0%, 0.30%, 0.15%,
0.15% or less, and a total of 1.5% or less.
【0019】Fe:不純物として含まれるFeは、Al
CuFe、Al12(Fe,Mn)Cu、(F
e,Mn)Al等の晶出物を生成する。これらの晶出
物は破壊靭性、疲労特性及び成形加工性に対して有害で
あり、Fe含有量が0.5%を越えると顕著に破壊靭
性、疲労特性及び成形性が低下するため、Fe含有量は
0.5%以下とする。なお、晶出物としては、Fe系以
外のAlCuMg、AlCu、MgSi等の
可溶のものがあり、これらは溶体化処理及び焼入れで十
分にAlマトリックス中に再固溶させることが望まし
い。 その他の不純物:Niは0.05%以下に制限する。
Fe: Fe contained as impurities is Al
7 Cu 2 Fe, Al 12 (Fe, Mn) 3 Cu 2 , (F
e, Mn) generating a crystallized substances such as Al 6. These precipitates are harmful to fracture toughness, fatigue properties, and formability. If the Fe content exceeds 0.5%, fracture toughness, fatigue properties, and formability are significantly reduced. The amount is 0.5% or less. In addition, as a crystallized substance, there are soluble substances such as Al 2 Cu 2 Mg, Al 2 Cu 2 , and Mg 2 Si other than Fe-based substances, and these are sufficiently reconstituted in the Al matrix by solution treatment and quenching. It is desirable to form a solid solution. Other impurities: Ni is limited to 0.05% or less.
【0020】[0020]
【実施例】以下、本発明の実施例を説明する。 (実施例1)Mg:0.5%、Si:1.2%、Mn:
0.05%、Fe:0.15%、Cr:0.01%、N
i:0.001%、Zn:0.03%、Cu:0.03
%、Ti:0.06%、Bi:10ppm、Be:30
ppmを含み、残部Al及び不純物からなるアルミニウ
ム合金を溶解鋳造し、480mm厚の鋳塊とし、次に5
40℃×8hrの均質化熱処理を行った後、粗熱間圧延
(リバース)及び仕上げ連続熱延(4タンデム)で、
3.5mm厚の板としてコイルに巻き上げ、中間焼鈍を
行い又は行わず、冷間圧延で1.2mm厚の板とした
後、溶体化処理及び焼入れを行った。溶体化処理及び焼
入れは、連続焼鈍で400℃まで平均昇温速度300℃
/分で加熱後、550℃まで約1分間でさらに加熱した
後、強制空冷で30℃まで平均冷却速度40℃/分で冷
却した。各工程の処理条件は表1に示す。
Embodiments of the present invention will be described below. (Example 1) Mg: 0.5%, Si: 1.2%, Mn:
0.05%, Fe: 0.15%, Cr: 0.01%, N
i: 0.001%, Zn: 0.03%, Cu: 0.03
%, Ti: 0.06%, Bi: 10 ppm, Be: 30
ppm, and an aluminum alloy consisting of the balance Al and impurities was melt-cast into a 480 mm thick ingot,
After performing homogenizing heat treatment at 40 ° C. × 8 hr, rough hot rolling (reverse) and finish continuous hot rolling (4 tandem)
A 3.5 mm-thick plate was wound around a coil, subjected to intermediate annealing or not, and cold-rolled into a 1.2 mm-thick plate, followed by solution treatment and quenching. Solution treatment and quenching are performed at an average temperature increase rate of 300 ° C to 400 ° C by continuous annealing.
After heating at 550 ° C. for about 1 minute, the mixture was cooled to 30 ° C. by forced air cooling at an average cooling rate of 40 ° C./min. Table 1 shows the processing conditions of each step.
【0021】[0021]
【表1】 [Table 1]
【0022】この板からサンプリングを行い、各材料特
性を下記要領で測定した。 ミクロ結晶粒;再結晶の粒径は、サンプリングした板材
について、L方向の結晶粒径(dL)及びLT方向の結
晶粒径(dLT)はL−LT面(表層部位を0.1mm研
磨)を、ST方向の結晶粒径(dST)はL−ST面を機
械研磨した後、電解エッチング(テトラフルオロほう
酸:水=15:400、電圧30V、溶液温度20〜3
0℃、エッチング時間60〜90秒)し、光学顕微鏡
(偏光板使用、倍率50倍)を用いて、ラインインター
セプト法(JISH0501準拠)にて評価した。 引張特性;焼入れ後の板を室温で3カ月時効後、JIS
−Z2241に準拠し、常温大気中でJIS5号試験片
を用いて、LT方向(圧延方向に対して90゜方向)に
引張速度5mm/分にて行った。
Sampling was performed from this plate, and each material property was measured in the following manner. Micro crystal grains: The recrystallized grain size was determined by measuring the L-LT surface (the surface layer portion was polished by 0.1 mm) for the sampled plate material in terms of the L-direction crystal grain size (dL) and the LT direction crystal grain size (dLT). The crystal grain size (dST) in the ST direction is determined by mechanically polishing the L-ST surface, and then performing electrolytic etching (tetrafluoroboric acid: water = 15: 400, voltage 30 V, solution temperature 20 to 3).
The film was evaluated at 0 ° C. and an etching time of 60 to 90 seconds by an optical microscope (using a polarizing plate, magnification of 50 ×) by a line intercept method (based on JIS H0501). Tensile properties: After aging the quenched plate at room temperature for 3 months, JIS
Based on -Z2241, using a JIS No. 5 test piece in a normal temperature atmosphere, the test was performed in the LT direction (90 ° direction with respect to the rolling direction) at a tensile speed of 5 mm / min.
【0023】リジングマークの評価;製品板よりJIS
5号試験片(長手方向が圧延方向と直角、平行部の長さ
60mm)を作製後、平行部位をバフ研磨で鏡面状態と
した。これを15%の引張変形(ケージ長さ50mm、
変形速度5mm/分)した後、平行部位の板表面の凹凸
の程度を目視観察し、リジングマークが発生した場合を
×、リジングマークの判別困難な場合を○と評価した。
Evaluation of ridging mark; JIS from product plate
After preparing a No. 5 test piece (the longitudinal direction was perpendicular to the rolling direction and the length of the parallel portion was 60 mm), the parallel portion was mirror-finished by buffing. This is subjected to a 15% tensile deformation (cage length 50 mm,
After a deformation rate of 5 mm / min), the degree of unevenness of the plate surface at the parallel portion was visually observed, and a case where a ridging mark was generated was evaluated as x, and a case where it was difficult to distinguish the ridging mark was evaluated as ○.
【0024】表1から分かるように、サンプルの耳率が
−4%以上であったNo.1〜3及び6にはリジングマ
ークの発生がなかった。さらに再結晶粒のサイズが45
μm以下であったNo.1〜3にはオレンジピールの発
生もなかった。一方、耳率が−4%未満であったNo.
4、5にはリジングマークが発生した。
As can be seen from Table 1, the sample No. having an ear ratio of -4% or more. No ridging marks were generated in Nos. 1 to 3 and 6. Furthermore, the size of recrystallized grains is 45
No. which was less than μm. No orange peel was generated in 1 to 3. On the other hand, the ear ratio was less than -4%.
Ridging marks occurred on 4 and 5.
【0025】[0025]
【発明の効果】本発明によれば、熱延及び続いて必要に
応じて中間焼鈍を行った後冷延し、その後溶体化及び焼
入れ処理し、ミクロ組織を等軸状再結晶粒としたAl−
Mg−Si系アルミニウム合金板をカップ状に成形加工
したときに発生する耳率を規定することで、その製品板
における耐リジングマーク性を保証することができる。
また、製品板における耐リジングマーク性を短時間で確
実に評価できるので、その評価結果を製造工程に直ちに
反映させ、耐リジングマーク性に劣るアルミニウム合金
板が大量に製造される事態を防止することが可能とな
る。
According to the present invention, Al is hot-rolled, then, if necessary, is subjected to intermediate annealing, then cold-rolled, and then is subjected to a solution treatment and a quenching treatment so that the microstructure becomes equiaxed recrystallized grains. −
By defining the ear ratio generated when the Mg-Si-based aluminum alloy plate is formed into a cup shape, the ridging mark resistance of the product plate can be guaranteed.
In addition, since the ridging mark resistance of a product plate can be reliably evaluated in a short time, the result of the evaluation is immediately reflected in the manufacturing process to prevent a situation in which an aluminum alloy plate with poor ridging mark resistance is manufactured in large quantities. Becomes possible.
───────────────────────────────────────────────────── 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 1/00 604 C22F 1/00 604 630 630K 631 631Z ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) C22F 1/00 604 C22F 1/00 604 630 630K 631 631Z

Claims (5)

    【特許請求の範囲】[Claims]
  1. 【請求項1】 Si:0.2〜1.8%(mass%、
    以下同じ)、Mg:0.2〜1.6%を含有し、熱延及
    び続いて必要に応じて中間焼鈍を行った後冷延し、その
    後溶体化及び焼入れ処理されたAl−Mg−Si系アル
    ミニウム合金板であり、ミクロ組織が等軸状の再結晶粒
    からなり、さらに「直径40mmのポンチ(肩部半径3
    mm)及びポンチとダイスの隙間とAl合金板厚の比が
    1.3〜1.4の範囲のダイスを用い、しわ押え力15
    0kgf、成形速度60mm/分、使用潤滑油#70
    0」の条件でカップ状に成形加工したとき、カップ耳率
    が−4%以上であることを特徴とする耐リジングマーク
    性に優れたアルミニウム合金板。
    1. Si: 0.2 to 1.8% (mass%,
    The same applies hereinafter), Mg: 0.2 to 1.6%, Al-Mg-Si which is cold-rolled after hot rolling and, if necessary, intermediate annealing, and then solution-treated and quenched. -Based aluminum alloy plate, the microstructure of which is composed of equiaxed recrystallized grains, and a punch having a diameter of 40 mm (shoulder radius 3
    mm) and a die having a ratio between the gap between the punch and the die and the thickness of the Al alloy in the range of 1.3 to 1.4, and a wrinkle holding force of 15 mm.
    0 kgf, molding speed 60 mm / min, lubricating oil used # 70
    An aluminum alloy sheet having excellent ridging mark resistance, wherein the cup ear ratio is -4% or more when formed into a cup under the condition of "0".
  2. 【請求項2】 45μm以下の結晶粒径を有する請求項
    1に記載された耐リジングマーク性に優れたアルミニウ
    ム合金板。
    2. The aluminum alloy sheet having excellent ridging mark resistance according to claim 1, which has a crystal grain size of 45 μm or less.
  3. 【請求項3】 Al−Mg−Si系アルミニウム合金
    が、さらにZn:0.005〜1.0%、Cu:0.
    005〜1.0%、Ti:0.001〜0.1%の1種
    又は2種以上、B:1〜300ppm、Be:0.1
    〜100ppmの1種又は2種、Mn:1.0%以
    下、Cr:0.3%以下、Zr:0.15%以下、V:
    0.15%以下のうちより1種又は2種以上を合計で
    0.01〜1.5%、以上〜のいずれか又はこれら
    を組み合わせて含有することを特徴とする、請求項1又
    は2に記載された耐リジングマーク性に優れた成形加工
    用板材が得られるアルミニウム合金板。
    3. The Al-Mg-Si-based aluminum alloy further contains 0.005% to 1.0% of Zn and 0.1% of Cu.
    005 to 1.0%, one or more of Ti: 0.001 to 0.1%, B: 1 to 300 ppm, Be: 0.1
    1 to 2 ppm of Mn: 1.0% or less, Cr: 0.3% or less, Zr: 0.15% or less, V:
    3. The method according to claim 1, wherein one or more of 0.15% or less are contained in a total of 0.01 to 1.5%, and any one or more of these or a combination thereof. 4. An aluminum alloy sheet from which the sheet material for forming process having excellent ridging mark resistance described can be obtained.
  4. 【請求項4】 自動車パネル用であることを特徴とする
    請求項1〜3のいずれかに記載された耐リジングマーク
    性に優れた成形加工用板材が得られるアルミニウム合金
    板。
    4. An aluminum alloy sheet from which the sheet material for forming process excellent in ridging mark resistance according to claim 1 is obtained for an automotive panel.
  5. 【請求項5】 Si:0.2〜1.8%、Mg:0.2
    〜1.6%を含有し、熱延及び続いて必要に応じて中間
    焼鈍を行った後冷延し、その後溶体化及び焼入れ処理さ
    れたAl−Mg−Si系アルミニウム合金板について、
    カップ状に絞り成形してその耳高さを測定することを特
    徴とする、Al−Mg−Si系アルミニウム合金板の耐
    リジングマーク性の評価方法。
    5. Si: 0.2-1.8%, Mg: 0.2
    About 1.6%, the Al-Mg-Si-based aluminum alloy sheet which was cold-rolled after being subjected to hot rolling and, if necessary, intermediate annealing as needed, and then subjected to solution treatment and quenching treatment,
    A method for evaluating the ridging mark resistance of an Al-Mg-Si-based aluminum alloy plate, which comprises forming the cup in a cup shape and measuring its ear height.
JP27009398A 1998-09-24 1998-09-24 Aluminum alloy plate with excellent ridging mark resistance and method for evaluating the occurrence of ridging mark Expired - Lifetime JP3498942B2 (en)

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Cited By (9)

* Cited by examiner, † Cited by third party
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JP2002018696A (en) * 2000-06-14 2002-01-22 Alcoa Inc Method for smoothing surface of aluminum or aluminum alloy used as aircraft part and such aircraft part
KR100569454B1 (en) 2004-10-12 2006-04-07 현대자동차주식회사 Method of manufacturing al-mg-si alloy sheet
JP2007077472A (en) * 2005-09-15 2007-03-29 Kobe Steel Ltd Aluminum alloy sheet having excellent formability, and its production method
JP2007203348A (en) * 2006-02-02 2007-08-16 Nissan Motor Co Ltd Method of producing molding die
KR100857681B1 (en) * 2006-12-28 2008-09-08 주식회사 포스코 method of manufacturing a ferritic stainless steel with improved ridging property
US8366846B2 (en) 2008-03-31 2013-02-05 Kobe Steel, Ltd. Aluminum alloy sheet with excellent post-fabrication surface qualities and method of manufacturing same
JP2014218734A (en) * 2013-04-09 2014-11-20 株式会社神戸製鋼所 Aluminum alloy sheet for press molding, manufacturing method therefor and press molded body thereof
CN104789830A (en) * 2014-05-30 2015-07-22 安徽鑫发铝业有限公司 Acid-resistant aluminum alloy section
WO2019189517A1 (en) * 2018-03-30 2019-10-03 株式会社神戸製鋼所 Aluminum alloy sheet for automotive structural member, automotive structural member, and method for manufacturing aluminum alloy sheet for automotive structural member

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002018696A (en) * 2000-06-14 2002-01-22 Alcoa Inc Method for smoothing surface of aluminum or aluminum alloy used as aircraft part and such aircraft part
KR100569454B1 (en) 2004-10-12 2006-04-07 현대자동차주식회사 Method of manufacturing al-mg-si alloy sheet
JP2007077472A (en) * 2005-09-15 2007-03-29 Kobe Steel Ltd Aluminum alloy sheet having excellent formability, and its production method
JP4515363B2 (en) * 2005-09-15 2010-07-28 株式会社神戸製鋼所 Aluminum alloy plate excellent in formability and method for producing the same
JP2007203348A (en) * 2006-02-02 2007-08-16 Nissan Motor Co Ltd Method of producing molding die
KR100857681B1 (en) * 2006-12-28 2008-09-08 주식회사 포스코 method of manufacturing a ferritic stainless steel with improved ridging property
US8366846B2 (en) 2008-03-31 2013-02-05 Kobe Steel, Ltd. Aluminum alloy sheet with excellent post-fabrication surface qualities and method of manufacturing same
JP2014218734A (en) * 2013-04-09 2014-11-20 株式会社神戸製鋼所 Aluminum alloy sheet for press molding, manufacturing method therefor and press molded body thereof
CN105102645A (en) * 2013-04-09 2015-11-25 株式会社神户制钢所 Aluminum alloy sheet for press forming, process for manufacturing same, and press-formed product thereof
CN104789830A (en) * 2014-05-30 2015-07-22 安徽鑫发铝业有限公司 Acid-resistant aluminum alloy section
WO2019189517A1 (en) * 2018-03-30 2019-10-03 株式会社神戸製鋼所 Aluminum alloy sheet for automotive structural member, automotive structural member, and method for manufacturing aluminum alloy sheet for automotive structural member

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