JP2823797B2 - Manufacturing method of aluminum alloy sheet for forming - Google Patents

Manufacturing method of aluminum alloy sheet for forming

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Publication number
JP2823797B2
JP2823797B2 JP6041850A JP4185094A JP2823797B2 JP 2823797 B2 JP2823797 B2 JP 2823797B2 JP 6041850 A JP6041850 A JP 6041850A JP 4185094 A JP4185094 A JP 4185094A JP 2823797 B2 JP2823797 B2 JP 2823797B2
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JP
Japan
Prior art keywords
less
temperature
aluminum alloy
forming
solution treatment
Prior art date
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JP6041850A
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Japanese (ja)
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JPH07228956A (en
Inventor
秀俊 内田
英雄 吉田
Original Assignee
住友軽金属工業株式会社
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Classifications

    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/06Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08Alloys based on aluminium with magnesium as the next major constituent with silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/02Alloys based on aluminium with silicon as the next major constituent
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions

Description

【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION
【0001】[0001]
【産業上の利用分野】本発明は、成形加工用アルミニウ
ム合金板の製造方法、とくに、高強度および良好なプレ
ス成形性を有し、成形加工後の表面外観が優れ、自動車
用外板など輸送機器用材料して好適な成形加工用アルミ
ニウム合金板の製造方法に関する。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an aluminum alloy sheet for forming and processing, and in particular, has a high strength and a good press formability, has an excellent surface appearance after forming, and is used for transportation of automobile outer panels. The present invention relates to a method for producing an aluminum alloy sheet for forming work suitable as a material for equipment.
【0002】[0002]
【従来の技術】近年、地球環境保護の観点から自動車な
ど輸送機器の軽量化が積極的に進められている。鉄鋼材
料からアルミニウム材料に転換して軽量化を図る動きも
活発で、自動車部材についても各種アルミニウム合金の
開発が行われている。自動車外板用アルミニウム合金と
しては、我が国では5000系のAl−Mg−Zn−C
u合金(特開昭53-103914 号公報、特開昭58-171547 号
公報) 、Al−Mg−Cu合金(特開平1-219139号公
報) の開発が進んでおり、一部実用化されているものも
ある。
2. Description of the Related Art In recent years, transport equipment such as automobiles has been actively reduced in weight from the viewpoint of protection of the global environment. There is an active movement to reduce weight by changing from steel to aluminum, and various aluminum alloys are also being developed for automotive components. As aluminum alloys for automobile outer panels, in Japan, 5000 series Al-Mg-Zn-C
U alloys (JP-A-53-103914, JP-A-58-171547) and Al-Mg-Cu alloys (JP-A-1-219139) have been developed and some of them have been commercialized. Some are.
【0003】欧米では6000系のAl−Mg−Si合
金、6009、6111、6016合金などが提案され
ている。6000系アルミニウム合金は、成形性は50
00系アルミニウム合金より幾分劣るものの自動車用外
板用としては十分な成形特性を備え、塗装焼付工程での
加熱処理により高強度が得られるため、5000系アル
ミニウム合金よりさらに薄肉化、軽量化が期待できる
が、成形加工後の表面外観が5000系合金に比べて劣
るという難点がある。
In the United States and Europe, 6000 series Al-Mg-Si alloys, 6009, 6111, 6016 alloys and the like have been proposed. 6000 series aluminum alloy has a formability of 50
Although it is somewhat inferior to the 00 series aluminum alloy, it has sufficient molding characteristics for automotive outer panels, and high strength can be obtained by heat treatment in the paint baking process, so it can be thinner and lighter than the 5000 series aluminum alloy. Although it can be expected, there is a disadvantage that the surface appearance after the forming process is inferior to that of the 5000 series alloy.
【0004】成形加工に伴って生じる代表的な欠陥とし
て、ストレッチャーストレインマーク(以下SSマーク
という)、オレンジピール(以下、肌荒れという)、リ
ジングマークがある。SSマークは、塑性加工時の降伏
点伸びが大きい材料に生じ易く、とくに5000系合金
で問題となることが多い。肌荒れは材料の結晶粒径が粗
大な場合に生じ易いことはよく知られている。リジング
マークは、結晶粒径が肌荒れを起こさない程度に細かい
場合であっても、その結晶学的方位の近い結晶粒が群れ
をなしているとその群れの境界で変形挙動が大きく異な
ることに起因して生じる表面の凹凸である。
[0004] Typical defects that occur during molding include a stretcher strain mark (hereinafter referred to as an SS mark), an orange peel (hereinafter referred to as a rough skin), and a ridging mark. The SS mark is easily generated in a material having a large yield point elongation at the time of plastic working, and is often a problem particularly in a 5000 series alloy. It is well known that rough skin is likely to occur when the crystal grain size of the material is large. Ridging marks are caused by the fact that even when the crystal grain size is small enough not to cause skin roughness, the deformation behavior at the boundary of the cluster is greatly different if the crystal grains with similar crystallographic orientation are in a cluster. This is the unevenness of the surface that occurs.
【0005】SSマークや肌荒れに対しては、それぞれ
レベラー矯正や結晶粒の微細化などの防止策が講じられ
ているが、リジングマークは、自動車外板のように成形
加工後より厳しい面質が要求される場合にのみ問題とさ
れるため、その防止策についてはこれまで十分な検討が
なされていなかった。6000系アルミニウム合金板を
自動車外板として成形加工する場合においてもリジング
マークの発生がしばしば観察され問題となっている。
For the SS mark and rough skin, measures have been taken to prevent the leveler from being corrected and the crystal grains to be refined, respectively. Since this is only a problem when required, preventive measures have not been sufficiently studied. Even when a 6000 series aluminum alloy plate is formed as an automobile outer plate, the occurrence of ridging marks is often observed and poses a problem.
【0006】[0006]
【発明が解決しようとする課題】本発明は、自動車外板
などの輸送機器用として5000系合金よりさらに薄肉
化、軽量化が期待できる6000系アルミニウム合金に
注目し、6000系合金における上記の問題点を解消す
るために、化学成分および製造条件と成形加工後の表面
欠陥とくにリジングマークとの関係について詳細に検討
を重ねた結果としてなされたものであり、その目的は、
高強度と良好な成形性を有し、且つ成形加工後の表面外
観が優れた成形加工用アルミニウム合金板の製造方法を
提供することにある。
SUMMARY OF THE INVENTION The present invention focuses on a 6000 series aluminum alloy which can be expected to be thinner and lighter than a 5000 series alloy for transportation equipment such as an automobile outer panel. In order to eliminate the points, it was made as a result of detailed examination of the relationship between chemical components and manufacturing conditions and surface defects after molding, especially ridging marks, the purpose of which is
An object of the present invention is to provide a method for producing an aluminum alloy sheet for forming, which has high strength and good formability, and has excellent surface appearance after forming.
【0007】[0007]
【課題を解決するための手段】上記の目的を達成するた
めの本発明による成形加工用アルミニウム合金板の製造
方法は、重量%で、Si:0.4%以上1.7%未満、
Mg:0.2以上1.2%未満を含み、残部Alと不可
避的不純物からなるアルミニウム合金鋳塊を、500℃
以上融点未満の温度で溶体化処理した後、500℃以上
の温度から350〜450℃の温度範囲まで冷却して熱
間圧延を開始し、該熱間圧延を200〜300℃の温度
範囲で終了し、溶体化処理直前に加工度50%以上の冷
間圧延を行い、該冷間圧延に引き続いて2℃/s以上の
昇温速度で500〜580℃の温度範囲に加熱し10分
以下の時間保持する溶体化処理を行った後、5℃/s以
上の冷却速度で100℃以下の温度に冷却することによ
り焼入れ処理することを構成上の第1の特徴とする。
In order to achieve the above object, a method of manufacturing an aluminum alloy sheet for forming according to the present invention is as follows: Si: 0.4% or more and less than 1.7% by weight;
Mg: an aluminum ingot containing 0.2 to less than 1.2%, the balance being Al and unavoidable impurities, was heated to 500 ° C.
After the solution treatment at a temperature lower than the melting point, the hot rolling is started by cooling from a temperature of 500 ° C. or more to a temperature range of 350 to 450 ° C., and the hot rolling is completed in a temperature range of 200 to 300 ° C. Immediately before the solution treatment, cold rolling is performed at a working ratio of 50% or more, and subsequent to the cold rolling, the material is heated to a temperature range of 500 to 580 ° C. at a heating rate of 2 ° C./s or more and heated for 10 minutes or less. The first feature of the structure is that the quenching treatment is performed by cooling to a temperature of 100 ° C. or less at a cooling rate of 5 ° C./s or more after performing the solution treatment for holding for a time.
【0008】また、アルミニウム合金鋳塊の組成を、S
i:0.4%以上1.7%未満、Mg:0.2%以上
1.2%未満を含み、さらにCu:1.0%以下、Z
n:1.0%以下、Mn:0.5%以下、Cr:0.2
%以下、Zr:0.2%以下、V:0.2%以下のうち
の1種または2種以上を含み、残部Alと不可避不純物
からなることを構成上の第2の特徴とする。
[0008] The composition of the aluminum alloy ingot is S
i: 0.4% or more and less than 1.7%, Mg: 0.2% or more and less than 1.2%, Cu: 1.0% or less, Z
n: 1.0% or less, Mn: 0.5% or less, Cr: 0.2
% Or less, Zr: 0.2% or less, V: 0.2% or less, and a second feature of the structure is that the balance is composed of Al and inevitable impurities.
【0009】さらに、重量%で、Si:0.8〜1.3
%、Mg:0.3〜0.8%を含み、残部Alと不可避
不純物からなるアルミニウム合金、またはSi:0.8
〜1.3%、Mg:0.3〜0.8%を含み、さらにC
u:1.0%以下、Zn:1.0%以下、Mn:0.5
%以下、Cr:0.2%以下、Zr:0.2%以下、
V:0.2%以下の1種または2種以上を含み、残部A
lと不可避的不純物からなるアルミニウム合金鋳塊を、
500℃以上融点未満の温度で均質化処理した後、50
0℃以上の温度から350〜400℃の温度範囲まで冷
却して熱間圧延を開始し、該熱間圧延を200〜250
℃の温度範囲で終了し、溶体化処理直前に加工度80%
以上の冷間圧延を行い、該冷間圧延に引き続いて昇温速
度2℃/s以上で500〜580℃の温度範囲に加熱し
1分以下の時間保持する溶体化処理を行った後、5℃/
s以上の冷却速度で100℃以下の温度に冷却すること
により焼入れ処理することを構成上の第3、第4の特徴
とする。
Further, by weight%, Si: 0.8 to 1.3.
%, Mg: an aluminum alloy containing 0.3 to 0.8% with the balance being Al and unavoidable impurities, or Si: 0.8%
1.3%, Mg: 0.3-0.8%, and further C
u: 1.0% or less, Zn: 1.0% or less, Mn: 0.5
% Or less, Cr: 0.2% or less, Zr: 0.2% or less,
V: one or more kinds of 0.2% or less, the balance A
l and an aluminum alloy ingot consisting of unavoidable impurities,
After homogenizing at a temperature of 500 ° C. or higher but lower than the melting point, 50
The hot rolling is started by cooling from a temperature of 0 ° C. or more to a temperature range of 350 to 400 ° C.
Finished in the temperature range of ℃, 80% workability just before solution treatment
After performing the cold rolling described above, and subsequent to the cold rolling, the solution is heated to a temperature range of 500 to 580 ° C. at a heating rate of 2 ° C./s or more and held for a time of 1 minute or less. ° C /
The third and fourth structural features are that the quenching process is performed by cooling to a temperature of 100 ° C. or less at a cooling rate of s or more.
【0010】本発明は、6000系アルミニウム合金に
おいて、成形加工性を低下させることなくリジングマー
クの発生を抑えるためには、合金組成を特定し、均質化
処理条件、熱間圧延条件、冷間加工度および最終溶体化
処理条件を厳密に管理することが必要であることを知見
したことに基づいてなされたものであり、その合金組成
において必須成分のSiは0.4%以上1.7%未満、
Mgは0.2%以上1.2%未満の範囲で含有させる。
SiとMgは共存してMg2Siを形成して合金の強度
を高める。Siが0.4%未満では十分な強度が得られ
ず、1.7%以上含有すると、合金をプレス加工する場
合加工時の耐力が高く成形性が劣る。また耐食性も劣化
する。Mgが0.2%未満では十分な強度が得られず、
1.2%以上では耐力が高く、成形性およびプレス加工
時にプレス型の形状が正確に現出できる特性、いわゆる
形状凍結性が劣化する。本発明のアルミニウム合金板
に、より優れた耐デント性および成形加工後の形状凍結
性を付与するためには、必須成分のSiを0.8〜1.
3%、Mgを0.3〜0.8%の範囲に限定するの好ま
しい。
According to the present invention, in order to suppress the occurrence of ridging marks in a 6000 series aluminum alloy without deteriorating formability, the alloy composition is specified, homogenization conditions, hot rolling conditions, cold working, It is based on the knowledge that it is necessary to strictly control the temperature and final solution treatment conditions, and the essential component Si in the alloy composition is 0.4% or more and less than 1.7%. ,
Mg is contained in a range of 0.2% or more and less than 1.2%.
Si and Mg coexist to form Mg 2 Si and increase the strength of the alloy. If the content of Si is less than 0.4%, sufficient strength cannot be obtained, and if the content is 1.7% or more, when the alloy is pressed, the yield strength during processing is high and the formability is poor. Also, the corrosion resistance deteriorates. If Mg is less than 0.2%, sufficient strength cannot be obtained,
If it is 1.2% or more, the proof stress is high, and the moldability and the characteristic that the shape of the press die can accurately appear at the time of press working, that is, the so-called shape freezing property deteriorates. In order to impart more excellent dent resistance and shape freezing after forming to the aluminum alloy sheet of the present invention, Si, which is an essential component, is contained in an amount of 0.8 to 1.
It is preferable to limit 3% and Mg to a range of 0.3 to 0.8%.
【0011】上記の必須合金成分の他に、選択成分とし
てCuを1.0%以下添加することによりさらに強度を
向上させることができる。Cuが1.0%を越えると耐
食性が低下し耐糸錆性も劣る。Znの添加も強度向上に
役立つが、1.0%を越えて含有すると耐食性が低下
し、また室温時効性が高くなるから、1.0%以下の範
囲で添加する。Mn:0.5%以下、Cr:0.2%以
下、Zr:0.2%以下およびV:0.2%以下の添加
は、合金の強度をさらに向上させるとともに結晶粒を微
細化して成形加工時の肌荒れ防止に効果がある。これら
の成分が上限を越えて添加されると粗大な金属間化合物
の生成が増加して成形性を劣化させる。
[0011] In addition to the above essential alloy components, the strength can be further improved by adding 1.0% or less of Cu as a selective component. If the Cu content exceeds 1.0%, the corrosion resistance is lowered and the rust resistance is poor. The addition of Zn also helps to increase the strength, but if it exceeds 1.0%, the corrosion resistance is reduced and the aging at room temperature is increased. Addition of Mn: 0.5% or less, Cr: 0.2% or less, Zr: 0.2% or less, and V: 0.2% or less further improves the strength of the alloy and refines the crystal grains to form the alloy. Effective in preventing rough skin during processing. If these components are added in excess of the upper limits, the formation of coarse intermetallic compounds increases and the formability deteriorates.
【0012】本発明においては、前記の各元素の他、鋳
塊の結晶粒微細化のためにTi:0.05%以下、また
はTi:0.05%以下およびB:100ppm以下を
添加してもよい。Ti、Bの添加量がそれぞれ上限を越
えると粗大な金属間化合物が増加し成形性が低下する。
不可避的不純物としてのFeは0.3%まで許容され
る。0.3%を越えると成形性とくに曲げ加工性が低下
する傾向がある。
In the present invention, in addition to the above-mentioned elements, Ti: 0.05% or less, or Ti: 0.05% or less and B: 100 ppm or less are added to refine the crystal grains of the ingot. Is also good. If the addition amounts of Ti and B exceed the respective upper limits, coarse intermetallic compounds increase and formability decreases.
Fe as an unavoidable impurity is allowed up to 0.3%. If it exceeds 0.3%, the moldability, particularly the bending workability, tends to decrease.
【0013】本発明のアルミニウム合金の製造条件につ
いて説明すると、半連続鋳造により前記の合金組成から
なるアルミニウム合金の鋳塊を製造し、鋳塊を500℃
以上、合金の溶融点未満の温度範囲で均質化処理する。
均質化処理温度が500℃より低いと、鋳塊偏析の除
去、合金組織の均質化が十分でなく、また強度に寄与す
るMg2 Si成分の固溶が不十分となり、成形性が劣る
場合がある。均質化処理後、室温まで冷却することなく
350〜450℃、より好ましくは350〜400℃の
温度範囲で熱間圧延を開始する。均質化処理後鋳塊を室
温まで冷却し熱間圧延温度に加熱した場合は、加熱時に
Mg2Siの粗大析出物が生成して溶体化処理での固溶
が困難となり成形性低下の原因となる。均質化処理後に
室温まで冷却した場合は、再度500℃以上の温度に加
熱した後350〜450℃、より好ましくは350〜4
00℃の範囲の温度に冷却して熱間圧延を開始すること
が必要である。
The conditions for producing the aluminum alloy of the present invention will be described. An ingot of an aluminum alloy having the above-mentioned alloy composition is produced by semi-continuous casting, and the ingot is heated to 500 ° C.
As described above, the homogenization treatment is performed in a temperature range lower than the melting point of the alloy.
If the homogenization treatment temperature is lower than 500 ° C., the ingot segregation is not sufficiently removed, the homogenization of the alloy structure is not sufficient, and the solid solution of the Mg 2 Si component contributing to the strength is insufficient, and the formability may be poor. is there. After the homogenization treatment, hot rolling is started at a temperature of 350 to 450 ° C, more preferably 350 to 400 ° C, without cooling to room temperature. When the ingot is cooled to room temperature and heated to the hot rolling temperature after the homogenization treatment, coarse precipitates of Mg 2 Si are generated during heating, so that solid solution in the solution treatment becomes difficult and the formability is reduced. Become. When cooled to room temperature after the homogenization treatment, it is heated again to a temperature of 500 ° C. or higher, and then 350 to 450 ° C., more preferably 350 to 450 ° C.
It is necessary to cool to a temperature in the range of 00 ° C. and start hot rolling.
【0014】熱間圧延は350〜450℃、より好まし
くは350〜400℃の温度範囲で開始し、200〜3
00℃、より好ましくは200〜250℃の温度範囲で
終了する。開始温度が350℃より低いと材料の変形抵
抗が大きく、450℃を越えると、熱間圧延時の組織が
大きく成長して冷間圧延および溶体化処理後の合金板に
結晶学的方位の近いものが群れをなし易いため、プレス
加工後の板材表面にリジングマークが生じ易い。熱間圧
延を300℃以上の温度で終了すると、圧延後に2次再
結晶が起こり易く組織が粗大化してリジングマーク発生
の原因となる。終了温度が200℃より低いと、水溶性
圧延油のステンが残り易く板材の表面品質を低下させ
る。
[0014] The hot rolling is started in a temperature range of 350 to 450 ° C, more preferably 350 to 400 ° C, and 200 to 3 ° C.
The process ends at a temperature of 00 ° C, more preferably 200 to 250 ° C. If the starting temperature is lower than 350 ° C., the deformation resistance of the material is large, and if it exceeds 450 ° C., the structure at the time of hot rolling grows greatly, and the crystallographic orientation is close to that of the alloy plate after cold rolling and solution treatment. Since the objects are likely to form a group, ridging marks are likely to be formed on the surface of the plate material after the press working. When the hot rolling is completed at a temperature of 300 ° C. or higher, secondary recrystallization is likely to occur after rolling, and the structure becomes coarse, which causes ridging marks. When the end temperature is lower than 200 ° C., the stainless steel of the water-soluble rolling oil is apt to remain, thereby deteriorating the surface quality of the sheet material.
【0015】熱間圧延終了後、必要に応じて中間焼鈍、
冷間圧延を行って所定の板厚とした後、溶体化処理直前
に加工度50%以上、より好ましくは80%以上の冷間
圧延を行い、冷間圧延に引き続いて溶体化処理を行う。
溶体化処理直前の冷間圧延の加工度が50%未満では、
溶体化処理後の結晶粒が粗大になり易く肌荒れが生じる
場合がある。また熱間圧延組織の分解が十分に行われ
ず、リジングマークが生じ易くなり成形性を低下させる
原因となる。
After completion of the hot rolling, if necessary, intermediate annealing,
After performing cold rolling to a predetermined thickness, cold rolling is performed immediately before the solution treatment to a working ratio of 50% or more, more preferably 80% or more, and the solution treatment is performed subsequent to the cold rolling.
If the working ratio of the cold rolling immediately before the solution treatment is less than 50%,
The crystal grains after the solution treatment are likely to become coarse and the skin may be rough. In addition, the decomposition of the hot-rolled structure is not sufficiently performed, and ridging marks are easily generated, which causes a reduction in formability.
【0016】溶体化処理は、昇温速度2℃/s以上で5
00〜580℃の温度範囲に加熱する。昇温速度が2℃
/s未満では結晶粒が粗大化してプレス成形時に肌荒れ
が生じ易くなる。加熱温度が500℃より低いと、析出
物の固溶が不十分となり所定の強度、成形性が得られな
い。所定の強度、成形性が得られるとしてもきわめて長
時間の熱処理が必要となり工業的に好ましくない。58
0℃より高い温度に加熱すると局部的な共晶融解が生じ
易くなり成形性を劣化させる。保持時間は10分以下が
好ましく、保持時間が10分を越えると生産性が低下し
工業的に好ましくない。より好ましくは1分以下とす
る。加熱後5℃/s以上の冷却速度で100℃以下の温
度に冷却し焼入れを行う。冷却速度が5℃/s未満では
結晶粒界に粗大な化合物が析出して延性が低下し強度、
成形性を低下させる。
The solution treatment is performed at a heating rate of 2 ° C./s or more for 5 hours.
Heat to a temperature range of 00-580 ° C. Heating rate is 2 ℃
If it is less than / s, the crystal grains become coarse and the surface becomes rough during press molding. When the heating temperature is lower than 500 ° C., the solid solution of the precipitate is insufficient, and the predetermined strength and moldability cannot be obtained. Even if predetermined strength and moldability can be obtained, an extremely long heat treatment is required, which is not industrially preferable. 58
When heated to a temperature higher than 0 ° C., local eutectic melting is likely to occur and the formability is deteriorated. The holding time is preferably 10 minutes or less, and if the holding time exceeds 10 minutes, the productivity is lowered and is not industrially preferable. More preferably, it is 1 minute or less. After heating, it is cooled to a temperature of 100 ° C. or less at a cooling rate of 5 ° C./s or more, and quenching is performed. If the cooling rate is less than 5 ° C./s, coarse compounds are precipitated at the crystal grain boundaries to reduce ductility and strength,
Decreases moldability.
【0017】[0017]
【作用】本発明においては、優れた強度および成形性を
有するための材料組成を選択し、特定条件の鋳塊均質化
処理、熱間圧延、冷間圧延および溶体化処理を組合わせ
ることにより、成形性を低下させることなく、肌荒れの
生じない微細な結晶粒径とし且つ結晶学的方位をランダ
ムにして、成形加工後の表面状態を優れたものとする。
In the present invention, by selecting a material composition for having excellent strength and formability, and combining ingot homogenization processing, hot rolling, cold rolling and solution treatment under specific conditions, The surface state after the forming process is made excellent by reducing the formability, setting the fine crystal grain size that does not cause skin roughness, and randomizing the crystallographic orientation.
【0018】[0018]
【実施例】以下、本発明の実施例を比較例と対比して説
明する。 実施例1 Si:1.2wt%、Mg:0.6wt%、Mn:0.1wt%、Fe:0.2wt%、Al
残部からなるアルミニウム合金の鋳塊を半連続鋳造によ
り製造し、得られた鋳塊を表面切削後、表1に示す製造
条件に従って処理し厚さ1mm厚の板材とした。これら
の板材について、引張試験を行い、200mm角のパネ
ルをプレス成形した後のリジングマーク、肌荒れ、SS
マークの発生を目視観察し、粒間腐食試験を行った。ま
た自動車用外板などに適用した場合の塗装焼付け処理を
想定して200℃で30分の熱処理を行った後の耐力
(BH後耐力)も測定した。試験、観察結果を表2に示
す。表2にみられるように、本発明に従って製造された
試験材は、いずれも成形前の耐力100MPa以上、伸
び率28%以上の優れた強度特性を有し、BH後の耐力
に優れ、成形加工後の表面外観も良好であり、粒間腐食
試験においても腐食深さ0.1mm以下で優れた耐食性
を示した。
Hereinafter, examples of the present invention will be described in comparison with comparative examples. Example 1 Si: 1.2 wt%, Mg: 0.6 wt%, Mn: 0.1 wt%, Fe: 0.2 wt%, Al
An aluminum alloy ingot consisting of the remaining portion was manufactured by semi-continuous casting, and the obtained ingot was subjected to surface cutting and then processed according to the manufacturing conditions shown in Table 1 to obtain a 1 mm thick plate. Tensile tests were performed on these plate materials, and ridging marks, rough surfaces, and SS
The occurrence of marks was visually observed, and an intergranular corrosion test was performed. The proof stress (after-BH proof stress) after heat treatment at 200 ° C. for 30 minutes was also measured assuming a paint baking treatment when applied to an automobile outer panel or the like. Table 2 shows the test and observation results. As can be seen from Table 2, all of the test materials manufactured according to the present invention have excellent strength properties of not less than 100 MPa in proof stress and not less than 28% in elongation, and have excellent proof stress after BH. The surface appearance after that was also good, and in the intergranular corrosion test, excellent corrosion resistance was exhibited at a corrosion depth of 0.1 mm or less.
【0019】[0019]
【表1】 [Table 1]
【0020】[0020]
【表2】 [Table 2]
【0021】比較例1 実施例1と同一組成のアルミニウム合金の鋳塊を半連続
鋳造により製造した。得られた鋳塊を表3に示す製造条
件に従って処理し、厚さ1mmの板材とした。これらの
板材について、実施例1と同様の試験を行った。結果を
表4に示す。なお、本発明の条件を外れたものには下線
を付した。
Comparative Example 1 An ingot of an aluminum alloy having the same composition as in Example 1 was produced by semi-continuous casting. The obtained ingot was processed according to the manufacturing conditions shown in Table 3 to obtain a plate having a thickness of 1 mm. The same test as in Example 1 was performed on these plate materials. Table 4 shows the results. In addition, those which deviate from the conditions of the present invention are underlined.
【0022】[0022]
【表3】 《表注》 540×8-RTは540 ℃で8h加熱後室温まで冷却
し、室温から再度380 ℃に加熱
[Table 3] 《Table Note》 540 × 8-RT is heated at 540 ° C for 8h, then cooled to room temperature and heated from room temperature to 380 ° C again
【0023】[0023]
【表4】 [Table 4]
【0024】表4に示されるように、製造条件No.1、N
o.2は熱間圧延開始温度が高過ぎ、条件No.3は熱間圧延
終了温度が高過ぎるため、これらの条件に従って製造さ
れた試験材はいずれも成形加工後リジングマークが生じ
た。条件No.8は冷間圧延加工度が小さく試験材の熱間圧
延組織の分解が十分でないため、成形加工後リジングマ
ークが発生し、結晶粒粗大化により肌荒れも生じた。条
件No.9は溶体化処理時の昇温速度が遅すぎるため結晶粒
が粗大化しプレス成形により肌荒れが生じた。条件No.1
0 は均質化処理後室温に冷却し熱間圧延温度に再加熱し
たため、試験材は溶体化処理での合金元素の溶入が十分
でなく伸び率が低く成形性が劣る。条件No.11 は溶体化
処理温度が低過ぎるため、析出物の固溶が不十分で強
度、伸び率ともに劣っている。
As shown in Table 4, the manufacturing conditions No. 1 and N
In o.2, the hot rolling start temperature was too high, and in Condition No. 3, the hot rolling end temperature was too high, so that all of the test materials manufactured according to these conditions had ridging marks after forming. In condition No. 8, the degree of cold rolling was small and the hot rolled structure of the test material was not sufficiently decomposed, so that ridging marks were formed after the forming process, and coarsening was caused by coarsening of crystal grains. In condition No. 9, the rate of temperature rise during the solution treatment was too slow, so that the crystal grains became coarse and the surface was roughened by press molding. Condition No.1
Sample No. 0 was cooled to room temperature and reheated to the hot rolling temperature after the homogenization treatment, so that the test material did not have sufficient penetration of alloying elements in the solution treatment, and the elongation was low and the formability was poor. In condition No. 11, since the solution treatment temperature was too low, the solid solution of the precipitate was insufficient and both the strength and the elongation were inferior.
【0025】実施例2 表5に示す組成のアルミニウム合金鋳塊を半連続鋳造に
より製造し、得られた鋳塊を表面切削後、表1の製造条
件No.1に従って処理し、厚さ1mmの板材とした。これ
らの板材について、実施例1と同様の試験を行った。試
験結果を表6に示す。表6にみられるように、本発明に
従って製造された試験材A 〜G はいずれも耐力100M
Pa以上の高い強度、28%以上の伸び率を有し、成形
性および成形加工後の表面外観においても優れていた。
粒間腐食試験も腐食深さ0.1mm以下で優れた耐食性
を示した。
Example 2 An aluminum alloy ingot having the composition shown in Table 5 was produced by semi-continuous casting, and the obtained ingot was subjected to surface cutting and then processed according to production condition No. 1 in Table 1 to obtain a 1 mm-thick ingot. Plate material was used. The same test as in Example 1 was performed on these plate materials. Table 6 shows the test results. As can be seen from Table 6, the test materials A to G manufactured according to the present invention all had a proof stress of 100M.
It had a high strength of Pa or more and an elongation of 28% or more, and was excellent in moldability and surface appearance after molding.
The intergranular corrosion test also showed excellent corrosion resistance at a corrosion depth of 0.1 mm or less.
【0026】[0026]
【表5】 [Table 5]
【0027】[0027]
【表6】 [Table 6]
【0028】比較例2 表7に示す組成のアルミニウム合金鋳塊を半連続鋳造に
より製造し、得られた鋳塊を表面切削後、表1の製造条
件No.1に従って処理し、厚さ1mmの板材とした。これ
らの板材について実施例1と同様の試験を行った結果を
表8に示す。表8にみられるように、合金H の試験材
は、Si、Mgの含有量が少ないため強度が低く、結晶粒も
大きく成形加工において肌荒れが生じた。合金I はMgの
含有量が少ないため強度が十分でなく、Cu量も多いため
粒間腐食試験における腐食深さが大きく耐食性が劣って
いる。合金J はSi含有量が多いため強度が増加し伸び率
が低下して十分な成形性が得られなかった。合金K はA5
182 合金で成形加工においてS-S マークが生じ表面外観
が損なわれた。なお、表7において本発明の条件を外れ
たものには下線を付した。
Comparative Example 2 An aluminum alloy ingot having a composition shown in Table 7 was produced by semi-continuous casting, and the obtained ingot was subjected to surface cutting and then processed according to production conditions No. 1 in Table 1 to obtain a 1 mm-thick ingot. Plate material was used. Table 8 shows the results of the same test as in Example 1 performed on these plate materials. As can be seen from Table 8, the test material of the alloy H 2 had low strength due to low contents of Si and Mg, and had large crystal grains, resulting in rough surface during molding. Alloy I has a low Mg content and thus has insufficient strength, and a large amount of Cu has a large corrosion depth in the intergranular corrosion test and poor corrosion resistance. Alloy J had a high Si content, so that the strength increased and the elongation decreased, and sufficient formability could not be obtained. Alloy K is A5
SS marks were formed in the forming process with 182 alloy, and the surface appearance was impaired. In Table 7, those outside the conditions of the present invention are underlined.
【0029】[0029]
【表7】 [Table 7]
【0030】[0030]
【表8】 [Table 8]
【0031】[0031]
【発明の効果】以上のとおり、本発明によれば、強度お
よび成形性とくにプレス成形性に優れ、成形加工後の表
面外観も良好で、自動車用外板をはじめとする輸送機器
部材の製造に好適な成形加工用アルミニウム合金板の製
造方法が提供される。
As described above, according to the present invention, excellent strength and moldability, particularly excellent press moldability, good surface appearance after molding, and the manufacture of transportation equipment members such as outer panels for automobiles. A method for manufacturing a suitable aluminum alloy sheet for forming is provided.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.6,DB名) C22F 1/04 - 1/057 C22C 21/00 - 21/18──────────────────────────────────────────────────続 き Continued on the front page (58) Field surveyed (Int. Cl. 6 , DB name) C22F 1/04-1/057 C22C 21/00-21/18

Claims (4)

    (57)【特許請求の範囲】(57) [Claims]
  1. 【請求項1】 重量%で、Si:0.4%以上1.7%
    未満、Mg:0.2%以上1.2%未満を含み、残部A
    lと不可避的不純物からなるアルミニウム合金鋳塊を、
    500℃以上融点未満の温度で均質化処理した後、50
    0℃以上の温度から350〜450℃の温度範囲まで冷
    却して熱間圧延を開始し、該熱間圧延を200〜300
    ℃の温度範囲で終了し、溶体化処理直前に加工度50%
    以上の冷間圧延を行い、該冷間圧延に引き続いて2℃/
    s以上の昇温速度で500〜580℃の温度範囲に加熱
    して10分以下の時間保持する溶体化処理を行った後、
    5℃/s 以上の冷却速度で100℃以下の温度まで冷
    却することにより焼入れ処理することを特徴とする成形
    加工用アルミニウム合金板の製造方法。
    1. Si: 0.4% or more and 1.7% by weight%
    , Mg: 0.2% or more and less than 1.2%, with the balance being A
    l and an aluminum alloy ingot consisting of unavoidable impurities,
    After homogenizing at a temperature of 500 ° C. or higher but lower than the melting point, 50
    It is cooled from a temperature of 0 ° C. or more to a temperature range of 350 to 450 ° C. to start hot rolling.
    Finished in a temperature range of ℃, and worked 50% immediately before solution treatment
    The above cold rolling is performed, and subsequently to the cold rolling, 2 ° C /
    After performing a solution treatment of heating to a temperature range of 500 to 580 ° C. at a temperature rising rate of s or more and holding for a time of 10 minutes or less,
    A method for producing an aluminum alloy sheet for forming, characterized by quenching by cooling to a temperature of 100 ° C or lower at a cooling rate of 5 ° C / s or higher.
  2. 【請求項2】 アルミニウム合金が、重量%で、Si:
    0.4%以上1.7%未満、Mg:0.2%以上1.2
    %未満を含み、Cu:1.0%以下、Zn:1.0%以
    下、Mn:0.5%以下、Cr:0.2%以下、Zr:
    0.2%以下およびV:0.2%以下のうちの1種また
    は2種以上を含み、残部Alと不可避的不純物からなる
    組成を有することを特徴とする請求項1記載の成形加工
    用アルミニウム合金板の製造方法。
    2. The method according to claim 1, wherein the aluminum alloy comprises Si:
    0.4% or more and less than 1.7%, Mg: 0.2% or more and 1.2
    %, Cu: 1.0% or less, Zn: 1.0% or less, Mn: 0.5% or less, Cr: 0.2% or less, Zr:
    The aluminum according to claim 1, characterized in that it contains one or more of 0.2% or less and V: 0.2% or less, and has a composition consisting of the balance of Al and inevitable impurities. Manufacturing method of alloy sheet.
  3. 【請求項3】 重量%で、Si:0.8〜1.3%、M
    g:0.3〜0.8%を含み、残部Alと不可避的不純
    物からなるアルミニウム合金鋳塊を、500℃以上融点
    未満の温度で均質化処理した後、500℃以上の温度か
    ら350〜400℃の温度範囲まで冷却して熱間圧延を
    開始し、該熱間圧延を200〜250℃の温度範囲で終
    了し、溶体化処理直前に加工度80%以上の冷間圧延を
    行い、該冷間圧延に引き続いて2℃/s以上の昇温速度
    で500〜580℃の温度範囲に加熱して1分以下の時
    間保持する溶体化処理を行った後、5℃/s以上の冷却
    速度で100℃以下の温度まで冷却することにより焼入
    れ処理することを特徴とする成形加工用アルミニウム合
    金板の製造方法。
    3. Si by weight: 0.8-1.3%, M
    g: An aluminum alloy ingot containing 0.3 to 0.8%, the balance being Al and unavoidable impurities, is homogenized at a temperature of 500 ° C. or more and less than the melting point, and then 350 to 400 ° C. from a temperature of 500 ° C. or more. C. to a temperature range of 200 ° C. to start hot rolling, finish the hot rolling in a temperature range of 200 to 250 ° C., and perform cold rolling at a working ratio of 80% or more immediately before solution treatment. Subsequent to the cold rolling, a solution treatment is performed by heating to a temperature range of 500 to 580 ° C. at a heating rate of 2 ° C./s or more and holding for a time of 1 minute or less, and then at a cooling rate of 5 ° C./s or more. A method for manufacturing an aluminum alloy sheet for forming, characterized by quenching by cooling to a temperature of 100 ° C. or lower.
  4. 【請求項4】 アルミニウム合金が、重量%で、Si:
    0.8〜1.3%、Mg:0.3〜0.8%を含み、C
    u:1.0%以下、Zn:1.0%以下、Mn:0.5
    %以下、Cr:0.2%以下、Zr:0.2%以下およ
    びV:0.2%以下のうちの1種または2種以上を含
    み、残部Alと不可避的不純物からなる組成を有するこ
    とを特徴とする請求項3記載の成形加工用アルミニウム
    合金板の製造方法。
    4. The method according to claim 1, wherein the aluminum alloy comprises Si:
    0.8-1.3%, Mg: 0.3-0.8%, C
    u: 1.0% or less, Zn: 1.0% or less, Mn: 0.5
    % Or less, Cr: 0.2% or less, Zr: 0.2% or less, and V: 0.2% or less, having a composition comprising the balance of Al and inevitable impurities. The method for producing an aluminum alloy sheet for forming according to claim 3, characterized in that:
JP6041850A 1994-02-16 1994-02-16 Manufacturing method of aluminum alloy sheet for forming Expired - Fee Related JP2823797B2 (en)

Priority Applications (1)

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JP6041850A JP2823797B2 (en) 1994-02-16 1994-02-16 Manufacturing method of aluminum alloy sheet for forming
PCT/JP1995/000200 WO1995022634A1 (en) 1994-02-16 1995-02-14 Method of manufacturing aluminum alloy plate for molding
EP95908373A EP0786535B2 (en) 1994-02-16 1995-02-14 Method of manufacturing aluminum alloy plate for forming
DE1995616297 DE69516297T3 (en) 1994-02-16 1995-02-14 METHOD FOR PRODUCING A COVER SHEET FROM ALUMINUM ALLOY FOR FORMING

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JPH07228956A JPH07228956A (en) 1995-08-29
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JPH07228956A (en) 1995-08-29
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