JP2003321754A - Method for manufacturing aluminum alloy sheet with excellent bendability - Google Patents
Method for manufacturing aluminum alloy sheet with excellent bendabilityInfo
- Publication number
- JP2003321754A JP2003321754A JP2002126338A JP2002126338A JP2003321754A JP 2003321754 A JP2003321754 A JP 2003321754A JP 2002126338 A JP2002126338 A JP 2002126338A JP 2002126338 A JP2002126338 A JP 2002126338A JP 2003321754 A JP2003321754 A JP 2003321754A
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- Japan
- Prior art keywords
- aluminum alloy
- treatment
- alloy
- alloy sheet
- ratio
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- 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.)
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- Shaping Metal By Deep-Drawing, Or The Like (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、板製造後に室温時
効が進んだ場合でも、特にヘム加工などの曲げ加工性に
優れ、プレス成形性や低温時効硬化能などの、パネル化
に際して要求される他の諸特性にも優れたAl-Mg-Si系ア
ルミニウム合金板(以下、アルミニウムを単にAlと言
う)に関するものである。TECHNICAL FIELD The present invention is excellent in bending workability such as hemming even when room temperature aging is advanced after plate production, and is required for panelization such as press formability and low temperature age hardening ability. The present invention relates to an Al-Mg-Si-based aluminum alloy plate (hereinafter, aluminum is simply referred to as Al) excellent in other various properties.
【0002】[0002]
【従来の技術】従来から、自動車、船舶あるいは車両な
どの輸送機、家電製品、建築、構造物の部材や部品用と
して、成形加工性 (以下、単に成形性と言う) に優れた
Al-Mg系のAA乃至JIS 規格に規定乃至相当する5000系
や、成形性や焼付硬化性に優れたAl-Mg-Si系のAA乃至JI
S 6000系 (以下、単に5000系乃至6000系と言う) のAl合
金材(圧延板材、押出形材、鍛造材などの各アルミニウ
ム合金展伸材を総称する)が使用されている。2. Description of the Related Art Conventionally, it has been excellent in moldability (hereinafter simply referred to as "formability") for transportation vehicles such as automobiles, ships or vehicles, home electric appliances, construction and structural members.
Al-Mg-based AA to 5000 system specified or equivalent to JIS standard, and Al-Mg-Si-based AA to JI excellent in moldability and bake hardenability
S 6000 series (hereinafter simply referred to as 5000 series to 6000 series) Al alloy materials (rolled sheet materials, extruded shape materials, forged materials and other aluminum alloy wrought materials are collectively referred to) are used.
【0003】近年、排気ガス等による地球環境問題に対
して、自動車などの輸送機の車体の軽量化による燃費の
向上が追求されている。このため、特に、自動車の車体
に対し、従来から使用されている鋼材に代わって、より
軽量なAl合金材の適用が増加しつつある。In recent years, in response to global environmental problems caused by exhaust gas and the like, improvement in fuel consumption has been pursued by reducing the weight of vehicle bodies of transportation machines such as automobiles. For this reason, in particular, the application of lighter Al alloy materials to the body of automobiles is increasing in place of the steel materials that have been conventionally used.
【0004】このAl合金材の中でも、自動車のフード、
フェンダー、ドア、ルーフ、トランクリッドなどのパネ
ル構造体の、アウタパネル (外板) やインナパネル( 内
板)等のパネルには、薄肉でかつ高強度Al合金板とし
て、過剰Si型の6000系のAl合金板の使用が検討されてい
る。Among these Al alloy materials, automobile hoods,
For panels such as outer panels (outer plates) and inner panels (inner plates) of panel structures such as fenders, doors, roofs, and trunk lids, a thin, high-strength Al alloy plate is used as an excess Si type 6000 series. The use of Al alloy plates is being considered.
【0005】この過剰Si型の6000系Al合金は、基本的に
は、Si、Mgを必須として含み、かつSi/Mg が1 以上であ
るAl-Mg-Si系アルミニウム合金である。そして、この過
剰Si型6000系Al合金は優れた時効硬化能を有しているた
め、プレス成形や曲げ加工時には低耐力化により成形性
を確保するとともに、成形後のパネルの塗装焼付処理な
どの、比較的低温の人工時効処理時の加熱により時効硬
化して耐力が向上し、必要な強度を確保できる時効硬化
能がある。This excess Si type 6000 series Al alloy is basically an Al-Mg-Si series aluminum alloy which essentially contains Si and Mg and has Si / Mg of 1 or more. And since this excess Si type 6000 series Al alloy has excellent age hardening ability, it secures formability by low yield strength at the time of press forming and bending, and at the same time, such as paint baking treatment of the panel after forming. The material has an age hardening ability capable of ensuring the required strength by age hardening by heating at the time of artificial aging treatment at a relatively low temperature to improve the yield strength.
【0006】また、これら過剰Si型6000系Al合金材は、
Mg量などの合金量が多い、他の5000系のAl合金などに比
して、合金元素量が比較的少ない。このため、これら60
00系Al合金材のスクラップを、Al合金溶解材 (溶解原
料) として再利用する際に、元の6000系Al合金鋳塊が得
やすく、リサイクル性にも優れている。Further, these excess Si type 6000 series Al alloy materials are
Compared to other 5000 series Al alloys, which have a large amount of alloys such as Mg, the amount of alloying elements is relatively small. Because of this, these 60
When the scrap of 00 series Al alloy material is reused as the Al alloy melting material (melting raw material), the original 6000 series Al alloy ingot is easily obtained and the recyclability is excellent.
【0007】しかし、これら過剰Si型6000系Al合金材
は、その優れた時効硬化能ゆえに、Al合金材自体の製造
後、前記各用途に使用されるまでの間に、大きな室温
(常温)時効が生じるという問題がある。However, because of their excellent age hardening ability, these excess Si type 6000 series Al alloy materials have a large room temperature after the Al alloy materials themselves are manufactured and before they are used for each of the above-mentioned applications.
(At room temperature) There is a problem that aging occurs.
【0008】例えば、この室温時効によって、過剰Si型
6000系Al合金材自体の製造後2 週間経過後でも、10% 程
度以上耐力が上昇するような現象も生じる。[0008] For example, due to this room temperature aging, excess Si type
Even after 2 weeks from the production of the 6000 series Al alloy material itself, the phenomenon that the yield strength increases by about 10% or more occurs.
【0009】そして、このような室温時効が生じた場
合、製造直後には、過剰Si型6000系Al合金板が前記各用
途の要求特性を満足したとしても、一定時間の経過後
に、実際の用途に使用される際には、前記要求特性を満
足できない問題を生じる。即ち、特にヘム加工性などの
曲げ加工性を著しく低下させ、また、前記プレス成形性
や前記比較的低温での時効硬化性などの他の諸特性も低
下させ、パネルとしての必要な形状精度や強度が得られ
ないこととなる。When such room temperature aging occurs, immediately after manufacturing, even if the excess Si type 6000 series Al alloy plate satisfies the required characteristics for each of the above-mentioned applications, after a certain period of time, it is actually used. When it is used for, the above-mentioned required characteristics cannot be satisfied. That is, in particular, the bending workability such as hemming workability is remarkably lowered, and other various properties such as the press formability and the age hardening at a relatively low temperature are also lowered, and the required shape accuracy as a panel and The strength cannot be obtained.
【0010】これに対し、本出願人は、特願2001-36670
0 号、特願2001-366701 号等により、過剰Si型を含む60
00系Al合金材の集合組織に、アルミニウム合金板に表面
における{200 }面の積分強度の割合が70% 以上である
とともに{200 }面と{400}面との合計積分強度の割
合が80% 以上であるような、異方性を有する集合組織
(キューブ方位を有する結晶粒が多く存在する組織) と
し、室温時効したとしても、ヘム加工などの曲げ加工性
に特に優れ、プレス成形性や低温時効硬化能などの、パ
ネル化に際して要求される他の諸特性にも優れた6000系
Al合金板を提案した。On the other hand, the present applicant has filed Japanese Patent Application No. 2001-36670.
No. 0, Japanese Patent Application No. 2001-366701, etc.
In the texture of 00 series Al alloy material, the ratio of the integrated strength of {200} plane on the surface of the aluminum alloy plate is 70% or more and the ratio of the total integrated strength of {200} plane and {400} plane is 80%. % Or more, anisotropic texture
(Structure with many crystal grains having a cube orientation), even if it is aged at room temperature, it is particularly excellent in bending workability such as hemming, and it is required for panelization such as press formability and low temperature age hardening ability. 6000 series with excellent characteristics
An Al alloy plate was proposed.
【0011】これらの異方性を持たせた集合組織とすれ
ば、室温時効抑制のために従来から行われている、Mg-S
i クラスター (溶体化および焼入れ処理後の室温放置中
に形成される) の複雑な制御を行わずとも、ヘム加工な
どの曲げ加工性に特に優れ、低温時効硬化能などの諸特
性にも優れた6000系Al合金板を提供できる。[0011] With these textures having anisotropy, Mg-S, which has been conventionally used for suppressing room temperature aging,
Even without complicated control of i clusters (formed during room temperature after solution heat treatment and quenching), it is particularly excellent in bending workability such as hemming and has excellent properties such as low temperature age hardening ability. We can provide 6000 series Al alloy plates.
【0012】[0012]
【発明が解決しようとする課題】前記異方性を有する集
合組織を得るためには、常法による板の製造方法とは異
なり、高い圧下率での冷間圧延とともに、冷間圧延途中
で、中間焼鈍を加えることが好ましい。In order to obtain a texture having the above-mentioned anisotropy, unlike the conventional method for producing a plate, cold rolling with a high reduction ratio is performed, and during cold rolling, It is preferable to add intermediate annealing.
【0013】しかし、上記製造方法において製造した場
合、異方性を有する集合組織は得られるものの、製造条
件によっては、最終の溶体化および焼入れ処理後の6000
系Al合金板の結晶粒径が粗大化する場合がある。そし
て、このように、結晶粒径が粗大化した場合、プレス成
形によって、成形後のパネル構造体に、リジングマーク
などの表面の肌荒れ不良が生じ易いという、新たな問題
を生じる。また、結晶粒径があまり大きくなった場合、
フラットヘムなどのヘム加工性も低下させることとな
る。However, when manufactured by the above manufacturing method, an anisotropic texture is obtained, but depending on the manufacturing conditions, 6000 after the final solution heat treatment and quenching treatment.
The grain size of the Al-based alloy plate may become coarse. When the crystal grain size becomes coarse in this way, a new problem arises in that the panel structure after molding is apt to suffer from rough surface defects such as ridging marks due to press molding. Also, if the crystal grain size becomes too large,
It also reduces the processability of hem such as flat hem.
【0014】このリジングマークや肌荒れが生じた場
合、特に表面が美麗であることが要求される、外板 (ア
ウタ) 用などのパネル構造体では、外観不良となって使
用できない問題となる。また、このリジングマークや肌
荒れは、プレス成形直後には比較的目立たず、そのまま
パネル構造体として塗装工程に進んだ際に、この塗装後
に顕著となるというやっかいな問題もある。When this ridging mark or rough skin occurs, a panel structure for an outer panel or the like, which requires a particularly beautiful surface, has a poor appearance and cannot be used. Further, there is also a troublesome problem that the ridging marks and the rough surface are relatively inconspicuous immediately after the press molding, and become prominent after the coating when the panel structure is directly subjected to the coating process.
【0015】本発明はこの様な事情に着目してなされた
ものであって、その目的は、室温時効したとしても、ヘ
ム加工などの曲げ加工性に優れ、更にリジングマークや
肌荒れを抑制してプレス成形性にも優れた6000系Al合金
板の製造方法を提供しようとするものである。The present invention has been made in view of such circumstances, and its purpose is to have excellent bending workability such as hemming even when aged at room temperature, and to suppress ridging marks and rough skin. An object of the present invention is to provide a method for producing a 6000 series Al alloy sheet which is also excellent in press formability.
【0016】[0016]
【課題を解決するための手段】この目的を達成するため
に、本発明の請求項1 の要旨は、熱間圧延されたAl-Mg-
Si系アルミニウム合金板を、10〜50% の圧下率で冷間圧
延後、210 〜440 ℃の温度で焼鈍し、更に70% 以上の圧
下率で冷間圧延した後、溶体化および焼入れ処理し、ア
ルミニウム合金板の集合組織に異方性を持たせるととも
に、平均結晶粒径を50μm 以下とすることである。In order to achieve this object, the subject matter of claim 1 of the present invention is that hot-rolled Al-Mg-
A Si-based aluminum alloy sheet is cold-rolled at a reduction rate of 10 to 50%, annealed at a temperature of 210 to 440 ° C, cold-rolled at a reduction rate of 70% or more, and then solution-treated and quenched. The texture of the aluminum alloy plate should be anisotropic, and the average grain size should be 50 μm or less.
【0017】なお、本発明で言うAl合金板とは、冷間圧
延後、調質処理を施した後に室温時効した板 (圧延板)
を言う。したがって、上記各要件も、調質処理直後 (板
製造直後) ではなく、調質処理後 (板製造後) からプレ
ス成形乃至曲げ加工されるまでの任意の期間 (例えば板
製造後から 1カ月以上経過後) における、充分室温時効
したAl合金板の状態をさして言う。また、ここで言う調
質処理とは、主として溶体化および焼き入れ処理を言う
が、その後の任意の熱処理、例えば、後述する予備時効
処理や、更に必要により施す時効処理などの種々の調質
処理を含めたものを示す。The Al alloy sheet referred to in the present invention is a sheet which has been subjected to tempering treatment after cold rolling and then aged at room temperature (rolled sheet).
Say Therefore, each of the above requirements is not just after the tempering treatment (immediately after the plate production), but after the tempering treatment (after the plate production) until the press forming or bending process (for example, one month or more after the plate production. (After lapse of time) refers to the state of the Al alloy plate aged sufficiently at room temperature. Further, the tempering treatment here mainly refers to solution heat treatment and quenching treatment, but any heat treatment thereafter, for example, various tempering treatments such as a preliminary aging treatment described later and an aging treatment to be performed if necessary. Including.
【0018】なお、以下の説明は、特に過剰Si型6000系
Al合金板を中心に行う。本発明は過剰Si型以外のAl-Mg-
Si系乃至6000系のAl合金板にも、課題としては過剰Si型
ほど厳しくないものの、効果はあるため、本発明範囲に
含みうる。また、同じく、以下の曲げ加工性の説明は、
特にフラットヘムなどのヘム加工を中心に行うが、ヘム
加工性が良好であれば、加工 (変形) の機構が共通す
る、他のハット型曲げ加工や90度曲げ加工などの曲げ加
工性も良好となる。したがって、本発明は、ヘム加工以
外の曲げ加工にも適用でき、本発明範囲に含みうる。The following description will be made especially for the excess Si type 6000 series.
Mainly on the Al alloy plate. The present invention is Al-Mg- other than excess Si type
The Si-based or 6000-based Al alloy plate also has the effect, though not as severe as the excessive Si type, but can be included in the scope of the present invention because it has an effect. Similarly, the following description of bending workability is
Especially, hem processing such as flat hem is mainly performed, but if the hem processing is good, other hat-shaped bending processing and 90-degree bending processing that have the same processing (deformation) mechanism are also good. Becomes Therefore, the present invention can be applied to bending work other than hemming and can be included in the scope of the present invention.
【0019】本発明者らの検討の結果、前記した異方性
を有する集合組織、言い換えると、キューブ方位を有す
る結晶粒が多く存在する組織を得るための方法におい
て、溶体化および焼入れ処理後のAl合金板の平均結晶粒
径は、前記焼鈍工程 (冷延途中) 前の前半の冷間圧延の
圧下率と、前記焼鈍工程後で溶体化および焼入れ処理前
の後半の冷間圧延の圧下率とに相関することを知見し
た。As a result of the study conducted by the present inventors, in the method for obtaining the above-mentioned texture having anisotropy, in other words, the texture having a large number of crystal grains having the cube orientation, after solution treatment and quenching treatment, The average grain size of the Al alloy plate, the reduction ratio of the cold rolling in the first half before the annealing process (during cold rolling) and the reduction ratio of the cold rolling in the latter half before the solution treatment and quenching treatment after the annealing process. It was found to be correlated with.
【0020】冷間圧延自体は冷間圧延板に十分な歪みエ
ネルギーを蓄積し、焼鈍や溶体化を含む調質処理で、異
方性を有する集合組織を得るために重要な工程である。
このため、冷間圧延板に十分な歪みエネルギーを蓄積す
るために、冷間圧延の圧下率をできるだけ高くすること
が好ましい。しかし、前記焼鈍工程前の前半の冷間圧延
の圧下率を高くした場合、焼鈍や溶体化を含む調質処理
で、Al合金板の結晶粒が成長しやすくなり、結晶粒が粗
大化する傾向が見られる。The cold rolling itself is an important step for accumulating sufficient strain energy in the cold rolled sheet, and a tempering treatment including annealing and solution treatment to obtain an anisotropic texture.
Therefore, in order to accumulate sufficient strain energy in the cold-rolled sheet, it is preferable that the cold rolling reduction ratio be as high as possible. However, when the reduction rate of the cold rolling in the first half before the annealing step is increased, the tempering treatment including annealing and solution treatment facilitates the growth of the crystal grains of the Al alloy plate, and the crystal grains tend to become coarse. Can be seen.
【0021】本発明では、この結晶粒径の粗大化を防止
して、Al合金板の結晶粒径を50μm以下とし、プレス成
形後のパネル構造体表面のリジングマークや肌荒れを抑
制するために、前記焼鈍工程前の前半の冷間圧延の圧下
率を低くする。その一方で、前記焼鈍工程後で溶体化お
よび焼入れ処理前の後半の冷間圧延の圧下率を高くし
て、異方性を有する集合組織を得る。In the present invention, in order to prevent the coarsening of the crystal grain size, the crystal grain size of the Al alloy plate to be 50 μm or less, and to suppress ridging marks and rough skin on the surface of the panel structure after press molding, The reduction ratio of the cold rolling in the first half before the annealing step is lowered. On the other hand, the reduction ratio of the cold rolling in the latter half after the annealing process and before the solution treatment and quenching treatment is increased to obtain an anisotropic texture.
【0022】本発明では上記特性を発揮するために、Al
合金板の成分組成の観点から、請求項2 のように、Al合
金板が、Si:0.4〜1.3%、Mg:0.2〜1.2%、Mn:0.01 〜0.65
% 、Cu:0.001〜1.0%を含み、かつSi/Mg が質量比で1 以
上であり、残部がAlおよび不可避的不純物である組成か
らなることが好ましい。In the present invention, in order to exhibit the above characteristics, Al
From the viewpoint of the composition of the alloy plate, as in claim 2, the Al alloy plate contains Si: 0.4 to 1.3%, Mg: 0.2 to 1.2%, Mn: 0.01 to 0.65.
%, Cu: 0.001 to 1.0%, Si / Mg in a mass ratio of 1 or more, and the balance being Al and inevitable impurities.
【0023】本発明では異方性を有する集合組織とし
て、好ましくは、請求項3 に記載のように、アルミニウ
ム合金板に表面における{200 }面の積分強度の割合が
70% 以上であるとともに{200 }面と{400 }面との合
計積分強度の割合が80% 以上である組織とする。In the present invention, as the texture having anisotropy, preferably, as described in claim 3, the aluminum alloy plate has a ratio of integrated intensity of {200} planes on the surface thereof.
The structure is 70% or more and the ratio of the total integrated intensity of the {200} plane and the {400} plane is 80% or more.
【0024】本発明では、従来のように、Al合金板の圧
延方向に対して平行方向の0.2%耐力を140MPa以下の低強
度とせずとも、特にフラットヘムなどのヘム加工性や張
出成形性が優れる。この結果、室温時効後のAl合金板の
0.2%耐力を前記140MPaを越える高強度にすることがで
き、成形後のパネル塗装工程などにおける、160 ℃×20
分の低温人工時効硬化処理でも、170MPaを越えるような
高強度のパネルを得ることができる。According to the present invention, even if the 0.2% proof stress in the direction parallel to the rolling direction of the Al alloy plate is not made as low as 140 MPa or less as in the conventional case, heme workability such as flat hem and stretch formability can be achieved. Is excellent. As a result, the Al alloy plate after aging at room temperature
The 0.2% proof stress can be increased to a high strength exceeding the above 140MPa, and 160 ℃ × 20
Even with a low temperature artificial age hardening treatment for a minute, a high-strength panel exceeding 170 MPa can be obtained.
【0025】また、本発明Al合金板は、ヘム加工などの
曲げ加工性に特に優れ、プレス成形性や低温時効硬化能
などの、パネル化に際して要求される他の諸特性にも優
れるので、請求項4 のように、Al合金板が張出成形後に
ヘム加工される場合に適用されて好ましい。Further, the Al alloy sheet of the present invention is particularly excellent in bending workability such as hemming and is excellent in other various properties required for forming a panel, such as press formability and low temperature age hardening ability. As described in item 4, it is preferably applied when the Al alloy plate is hemmed after the stretch forming.
【0026】[0026]
【発明の実施の形態】(製造方法)本発明製造方法につい
て以下に説明する。プレス成形後のパネル構造体表面の
リジングマークや肌荒れを抑制し、異方性を有する集合
組織 (キューブ方位を有する結晶粒が多く存在する組
織) とするためにはAl合金板の製造において、常法とは
異なり、冷間圧延で弱圧延して、特定温度で焼鈍した
後、更に、冷間圧延で強圧延して、その後調質処理する
などの特別の工程が必要である。この点、常法で得られ
る通常のAl合金板は、キューブ方位を有する結晶粒の割
合が小さく、等方性組織であり、本発明のような異方性
を有する、あるいは異方性の強い集合組織とはならな
い。(Manufacturing Method) The manufacturing method of the present invention will be described below. In order to suppress ridging marks and skin roughness on the surface of the panel structure after press molding and to have an anisotropic texture (a structure in which many crystal grains having a cube orientation are present), it is usually used in the production of Al alloy plates. Unlike the method, a special process such as weak rolling by cold rolling, annealing at a specific temperature, strong rolling by cold rolling, and subsequent heat treatment is required. In this respect, a normal Al alloy plate obtained by a conventional method has a small proportion of crystal grains having a cube orientation, has an isotropic structure, has anisotropy as in the present invention, or has a strong anisotropy. It does not become a collective organization.
【0027】より具体的に、本発明では、結晶粒径の粗
大化を防止して、Al合金板の平均結晶粒径を50μm 以下
とし、プレス成形後のパネル構造体表面のリジングマー
クや肌荒れを抑制するために、先ず、前記焼鈍工程前の
前半の冷間圧延の圧下率は10〜50% 、好ましくは10〜40
% の範囲の比較的低い圧下率とする。More specifically, in the present invention, coarsening of the crystal grain size is prevented, the average crystal grain size of the Al alloy plate is set to 50 μm or less, and ridging marks and skin roughness on the surface of the panel structure after press molding are prevented. In order to suppress, first, the reduction ratio of the cold rolling in the first half before the annealing step is 10 to 50%, preferably 10 to 40%.
A relatively low rolling reduction in the range of%.
【0028】この圧下率が10% 未満では、前記焼鈍工程
後で溶体化および焼入れ処理前の後半の冷間圧延の圧下
率を高くしても、キューブ方位を有する結晶粒を後述す
る好ましい割合とするなど、異方性の強い集合組織を得
ることが難しい。When the rolling reduction is less than 10%, even if the rolling reduction in the latter half of the cold rolling after the annealing step and before the solution heat treatment and quenching is increased, the crystal grains having the cube orientation have a preferable ratio described below. It is difficult to obtain a highly anisotropic texture.
【0029】一方、この圧下率が50% を越えた場合、よ
り厳しくは40% を越えた場合、前記焼鈍工程後で溶体化
および焼入れ処理前の後半の冷間圧延の圧下率を高くし
ても、最終の溶体化および焼入れ処理後の6000系Al合金
板の結晶粒径が50μm を越えて粗大化する可能性が高
い。この結果、プレス成形によって、パネル構造体にリ
ジングマークや肌荒れが生じ易くなる。また、フラット
ヘムなどのヘム加工性も低下させることとなる。On the other hand, if the reduction ratio exceeds 50%, or more strictly exceeds 40%, the reduction ratio of the cold rolling in the latter half after the annealing step and before the solution treatment and quenching treatment is increased. However, there is a high possibility that the crystal grain size of the 6000 series Al alloy plate after the final solution heat treatment and quenching will exceed 50 μm and become coarse. As a result, ridging marks and rough skin are likely to occur on the panel structure by press molding. In addition, the processability of hem such as flat hem is also reduced.
【0030】次に、前記焼鈍工程後で溶体化および焼入
れ処理前の後半の冷間圧延の圧下率を70% 以上と高くし
て、異方性を有する集合組織を得る。後半の冷間圧延で
の圧下率をこのように高くすることで、冷間圧延板に十
分な歪みエネルギーを蓄積できる。この結果、後の溶体
化を含む調質処理で、キューブ方位を有する多くの結晶
粒を成長させることができ、異方性の強い集合組織を得
ることができる。Next, the reduction ratio of the cold rolling in the latter half after the annealing process and before the solution treatment and quenching treatment is increased to 70% or more to obtain an anisotropic texture. By increasing the reduction ratio in the latter half cold rolling in this way, sufficient strain energy can be accumulated in the cold rolled sheet. As a result, in the subsequent heat treatment including solution treatment, many crystal grains having a cube orientation can be grown and a highly anisotropic texture can be obtained.
【0031】この圧下率が70% 未満では、キューブ方位
を有する結晶粒が成長するに十分な歪みエネルギーが蓄
積できず、異方性を有する集合組織を得ることが難し
い。そして、好ましくは、Al合金パネル表面のキューブ
方位を有する結晶粒の割合を、Al合金板表面における
{200 }面の積分強度の割合を50% 以上とするととも
に、{200 }面と{400 }面との合計積分強度の割合を
60% 以上とすることができない。即ち、この圧下率が低
いと、常法材と変わりなくなり、後述する調質処理で、
前記伸びの異方性を有する組織ができない。なお、一方
で、冷間圧延での圧下率が高くなるほど、耳割れが生じ
るなど加工自体が困難となるので、圧下率の上限は95%
程度とするのが好ましい。If the rolling reduction is less than 70%, sufficient strain energy cannot be accumulated for growing crystal grains having a cube orientation, and it is difficult to obtain an anisotropic texture. And, preferably, the ratio of the crystal grains having the cube orientation on the Al alloy panel surface is 50% or more of the integrated strength ratio of the {200} plane on the Al alloy plate surface, and the {200} plane and the {400} plane. The ratio of the total integrated intensity with the surface
It cannot be more than 60%. That is, when this reduction rate is low, it does not differ from the ordinary method material, and in the tempering process described later,
A structure having anisotropy of elongation cannot be formed. On the other hand, the higher the reduction ratio in cold rolling, the more difficult the process itself such as the occurrence of edge cracks, so the upper limit of the reduction ratio is 95%.
It is preferably about the same.
【0032】上記冷間圧延途中の焼鈍 (中間焼鈍) は、
キューブ方位を有する微細な再結晶粒もしくは亜結晶粒
を特定量成長させ、最終の溶体化処理で、立方体方位が
発達し易くし、異方性を有する集合組織を得るために必
須の工程である。この効果を生じるために210 〜440 ℃
の温度で焼鈍する必要がある。なお、焼鈍の時間は1〜5
0時間とすることが好ましい。Annealing during the cold rolling (intermediate annealing) is
It is an essential step to grow a specific amount of fine recrystallized grains or sub-crystalline grains having a cube orientation and to make the cubic orientation easy to develop in the final solution treatment and to obtain an anisotropic texture. . 210-440 ° C to produce this effect
It is necessary to anneal at the temperature. The annealing time is 1 to 5
It is preferably 0 hours.
【0033】この焼鈍温度が210 ℃未満では、前半の冷
間圧延の低圧下率との関係で、キューブ方位を有する結
晶粒成長の効果がなく、異方性を有する集合組織とする
ことができない。そして、好ましくは、Al合金パネル表
面のキューブ方位を有する結晶粒の割合を、Al合金板表
面における{200 }面の積分強度の割合を70% 以上とす
るとともに、{200 }面と{400 }面との合計積分強度
の割合を80% 以上とすることができない。この結果、従
来のAl合金板の集合組織と大差がなくなり、フラットヘ
ムなどのヘム加工性の向上効果がない。When the annealing temperature is less than 210 ° C., the grain growth having the cube orientation is not effective due to the relationship with the low pressure reduction ratio of the cold rolling in the first half, and the anisotropic texture cannot be obtained. . And, preferably, the ratio of the crystal grains having the cube orientation on the surface of the Al alloy panel is such that the ratio of the integrated strength of the {200} plane on the surface of the Al alloy plate is 70% or more, and the {200} plane and the {400} plane are The ratio of the total integrated intensity with the plane cannot be 80% or more. As a result, there is not much difference from the texture of the conventional Al alloy plate, and there is no effect of improving the hem workability such as flat hem.
【0034】一方、焼鈍温度が440 ℃を越えた場合、平
均結晶粒径が50μm を越えて粗大化しやすく、プレス成
形によって、パネル構造体表面にリジングマークや肌荒
れが生じ易くなる。なお、この焼鈍は、バッチ炉、連続
焼鈍炉などの種々の炉を適宜用いて行うことができる。On the other hand, when the annealing temperature exceeds 440 ° C., the average crystal grain size exceeds 50 μm and the particles tend to be coarsened, and press molding tends to cause ridging marks and rough skin on the surface of the panel structure. Note that this annealing can be performed by appropriately using various furnaces such as a batch furnace and a continuous annealing furnace.
【0035】なお、本発明で言う平均結晶粒径とは、板
の圧延方向(L方向) の結晶粒の平均粒径である。測定方
法は、Al合金板の圧延方向(L方向) と板厚方向 (ST方
向) とを含む面を機械研磨した後に電解エッチングした
面を、光学顕微鏡を用いて観察し、表面、板厚の1/8 の
部分、板厚の2/8 の部分、板厚の3/8 の部分、板厚の4/
8 の部分の各部で、前記L 方向に、ラインインターセプ
ト法で測定する。1 測定ライン長さは0.95mmとし、1 視
野当たり各5 本で合計5 視野を観察して、結晶粒径を測
定して平均化し、平均結晶粒径とする。The average crystal grain size referred to in the present invention is the average grain size of the crystal grains in the rolling direction (L direction) of the plate. The measuring method was to observe the surface electrolytically etched after mechanically polishing the surface including the rolling direction (L direction) and the plate thickness direction (ST direction) of the Al alloy plate using an optical microscope, 1/8 part, 2/8 part of thickness, 3/8 part of thickness, 4 / of thickness
At each part of section 8, measure in the L direction by the line intercept method. The length of one measurement line is 0.95 mm, and a total of 5 fields of view are observed for each 5 fields, and the crystal grain sizes are measured and averaged to obtain the average crystal grain size.
【0036】また、異方性を有する集合組織として、特
にフラットヘムなどのヘム加工性の向上のために、Al合
金板結晶粒のキューブ方位につき、前記した通り、Al合
金板表面の{200 }面のX 線回折による積分強度の割合
を70% 以上とするとともに{200 }面と{400 }面との
X 線回折による合計積分強度の割合を80% 以上とするこ
とが好ましい。Further, as an anisotropic texture, particularly in order to improve the processability of hem such as flat hem, the cube orientation of the Al alloy plate crystal grains is, as described above, {200} on the surface of the Al alloy plate. The ratio of the integrated intensity by X-ray diffraction of the plane is set to 70% or more, and the {200} plane and the {400} plane
The ratio of the total integrated intensity by X-ray diffraction is preferably 80% or more.
【0037】{200 }面のX 線回折による積分強度の割
合が70% 未満でかつ、{200 }面と{400 }面とのX 線
回折による合計積分強度の割合が80% 未満では、従来の
Al合金板結晶粒組織と大差がなくなり、特にフラットヘ
ムなどのヘム加工性の向上効果が生じない可能性があ
る。When the ratio of the integrated intensity of the {200} plane by X-ray diffraction is less than 70% and the ratio of the total integrated intensity of the {200} plane and the {400} plane by X-ray diffraction is less than 80%, of
There is almost no difference from the crystal grain structure of the Al alloy plate, and there is a possibility that the effect of improving the hem processability such as flat hem may not occur.
【0038】一方、{200 }面の積分強度の割合が90%
を越えた場合、また、{200 }面と{400 }面との合計
積分強度の割合が95% を越えた場合、Al合金板の成分組
成などによっては、張出成形や絞り成形などのプレス成
形性が低下する可能性がある。この結果、プレス成形に
おける、特にアウタパネルなどとして重要な、形状精度
乃至形状凍結性などが著しく低下する可能性がある。こ
のため、ヘム加工性以外のプレス成形性などの他の特性
を低下させないためには、キューブ方位を有する結晶粒
の割合を、Al合金板表面における{200 }面の積分強度
の割合が70〜90% の範囲であるとともに、{200 }面と
{400 }面との合計積分強度の割合が80% 〜95% の範囲
にすることが更に好ましい。On the other hand, the ratio of the integrated intensity of the {200} plane is 90%.
When the total integrated strength of the {200} plane and the {400} plane exceeds 95%, depending on the component composition of the Al alloy plate, press forming such as bulging or drawing may occur. Moldability may decrease. As a result, in press molding, there is a possibility that shape accuracy or shape fixability, which is important particularly as an outer panel, may be significantly reduced. Therefore, in order to prevent deterioration of other properties such as press formability other than hemmability, the ratio of the crystal grains having a cube orientation should be 70 to 70% of the integrated strength of the {200} plane on the Al alloy plate surface. It is more preferable that it is in the range of 90% and the ratio of the total integrated intensity of the {200} plane and the {400} plane is in the range of 80% to 95%.
【0039】Al合金板の結晶粒のキューブ方位発達の程
度の測定は、X 線回折装置 (例えばリガクRAD-RCなど)
を用い、Al合金板の表面を前処理無しでそのまま計測す
る。標準サンプルとしては無配向性のAl試料を用い、こ
の標準サンプルに対する、{111 }面、{200 }面、
{220 }面、{311 }面、{222 }面、{400 }面、
{331 }面、{420 }面、{422 }面、の各面の積分強
度の総和A を求める。そして、このA に対する前記{20
0 }面の積分強度I1の比率(%) 、{200 }面と{400 }
面との合計の積分強度I2の比率(%) 、を各々の積分強度
の割合(%) とする。An X-ray diffractometer (for example, Rigaku RAD-RC) was used to measure the degree of cube orientation development of the crystal grains of the Al alloy plate.
Is used to measure the surface of the Al alloy plate as it is without pretreatment. A non-oriented Al sample was used as the standard sample, and the {111} plane, {200} plane, and
{220} plane, {311} plane, {222} plane, {400} plane,
The sum A of the integrated intensities of the {331} plane, {420} plane, and {422} plane is obtained. And the {20
Ratio (%) of integrated intensity I 1 of 0} plane, {200} plane and {400} plane
The ratio (%) of the total integrated intensity I 2 to the surface is defined as the ratio (%) of each integrated intensity.
【0040】本発明において、その他の製造工程の各条
件は常法で可であるが、アウタパネルなどとしての、フ
ラットヘム加工性や他の特性を向上させるための好まし
い条件もあり、以下に説明する。In the present invention, other conditions of other manufacturing steps can be performed by a conventional method, but there are preferable conditions for improving the flat hem processability and other characteristics as an outer panel, which will be described below. .
【0041】先ず、溶解、鋳造工程では、6000系成分規
格範囲内に溶解調整されたAl合金溶湯を、連続鋳造圧延
法、半連続鋳造法(DC鋳造法)等の通常の溶解鋳造法を
適宜選択して鋳造する。次いで、このAl合金鋳塊に均質
化熱処理を施した後、熱間圧延し、コイル状、板状など
の板形状に加工する。First, in the melting and casting process, an ordinary molten casting method such as a continuous casting rolling method or a semi-continuous casting method (DC casting method) is appropriately used for an Al alloy molten metal whose melting is adjusted within the 6000 series component standard range. Select and cast. Next, this Al alloy ingot is subjected to homogenizing heat treatment, and then hot rolled to be processed into a plate shape such as a coil shape or a plate shape.
【0042】前記冷間圧延後のAl合金板は、調質処理と
して、必須に溶体化および焼入れ処理される。溶体化お
よび焼入れ処理は、後の塗装焼き付け硬化処理などの人
工時効硬化処理によりGPゾーンなどの化合物相を十分粒
内に析出させるために重要な工程である。この効果を出
すための溶体化処理条件は、500 〜560 ℃の温度範囲で
行うのが好ましい。これによって、Al合金板の0.2%耐力
を140MPaを越える高強度にして、プレス成形やヘムなど
の曲げ加工後の塗装工程などにおける前記低温短時間の
人工時効硬化処理でも170MPaを越えるような高強度のパ
ネルとする。The Al alloy plate after the cold rolling is inevitably subjected to solution heat treatment and quenching as heat treatment. Solution treatment and quenching are important steps for precipitating a compound phase such as GP zone in the grains sufficiently by an artificial age hardening treatment such as a paint baking hardening treatment to be performed later. The solution treatment conditions for producing this effect are preferably in the temperature range of 500 to 560 ° C. As a result, the 0.2% proof stress of the Al alloy plate is made to have a high strength exceeding 140 MPa, and high strength exceeding 170 MPa even with the artificial aging hardening treatment at a low temperature for a short time in the coating process after bending such as press forming and hem. Panel.
【0043】溶体化処理後の焼入れの際には、冷却速度
は50℃/ 分以上の急冷とすることが好ましい。冷却速度
が50℃/ 分未満の遅い場合には、焼入れ後の強度が低く
なり、時効硬化能が不足し、前記低温短時間の低温での
人工時効処理により170MPa以上の高耐力を確保できな
い。Upon quenching after the solution treatment, the cooling rate is preferably a rapid cooling rate of 50 ° C./minute or more. When the cooling rate is slower than 50 ° C./min, the strength after quenching becomes low, the age hardening ability becomes insufficient, and the high yield strength of 170 MPa or more cannot be secured by the artificial aging treatment at a low temperature for a short time and at a low temperature.
【0044】また、粒界上にSi、MgSiなどが析出しやす
くなり、プレス成形やフラットヘム加工時の割れの起点
となり易く、これら成形性が低下する。この冷却速度を
確保するために、焼入れ処理は、ファンなどの空冷でも
よいが冷却速度が遅くなる可能性が大きく、ミスト、ス
プレー、浸漬等の水冷手段から選択して行うことが好ま
しい。Further, Si, MgSi, etc. are likely to be deposited on the grain boundaries, which easily becomes a starting point of cracks during press molding or flat hem processing, and these moldability are deteriorated. In order to secure this cooling rate, the quenching treatment may be performed by air cooling using a fan or the like, but the cooling rate is likely to be slow, and it is preferable to perform the quenching treatment by selecting from water cooling means such as mist, spraying and dipping.
【0045】本発明では、成形パネルの塗装焼き付け工
程などの人工時効硬化処理での時効硬化性を高めるた
め、溶体化焼入れ処理後のクラスターの生成を抑制し、
GPゾーンの析出を促進するために、予備時効処理をして
も良い。この予備時効処理は、50〜100 ℃、好ましくは
60〜90℃の温度範囲に、1 〜24時間の必要時間保持する
ことが好ましい。また、予備時効処理後の冷却速度は、
1 ℃/hr 以下であることが好ましい。In the present invention, in order to enhance the age hardenability in the artificial age hardening treatment such as the paint baking process of the molded panel, the formation of clusters after the solution hardening treatment is suppressed,
A pre-aging treatment may be performed to accelerate the precipitation in the GP zone. This pre-aging treatment is performed at 50 to 100 ° C, preferably
It is preferable to maintain the temperature range of 60 to 90 ° C. for the required time of 1 to 24 hours. The cooling rate after the preliminary aging treatment is
It is preferably 1 ° C./hr or less.
【0046】この予備時効処理として、溶体化処理後の
焼入れ終了温度を50〜100 ℃と高くした後に、直ちに再
加熱乃至そのまま保持して行う。あるいは、溶体化処理
後常温までの焼入れ処理の後に、直ちに50〜100 ℃に再
加熱して行う。As the preliminary aging treatment, after the quenching completion temperature after the solution treatment is raised to 50 to 100 ° C., it is immediately reheated or kept as it is. Alternatively, after the solution treatment, quenching treatment up to room temperature and immediately reheating to 50 to 100 ° C. are performed.
【0047】また、連続溶体化焼入れ処理の場合には、
前記予備時効の温度範囲で焼入れ処理を終了し、そのま
まの高温でコイルに巻き取るなどして行う。なお、コイ
ルに巻き取る前に再加熱しても、巻き取り後に保温して
も良い。また、常温までの焼入れ処理の後に、前記温度
範囲に再加熱して高温で巻き取るなどしてもよい。In the case of continuous solution hardening treatment,
The quenching process is completed within the temperature range of the preliminary aging, and the coil is wound around the coil at the high temperature as it is. Note that the coil may be reheated before being wound on the coil, or may be kept warm after being wound. Further, after the quenching treatment up to room temperature, it may be reheated to the above temperature range and wound at a high temperature.
【0048】更に、室温時効抑制のために、前記予備時
効処理後に、時間的な遅滞無く、比較的低温での熱処理
(人工時効処理) を行い、GPゾーンを更に生成させても
良い。前記時間的な遅滞があった場合、予備時効処理後
でも、時間の経過とともに室温時効 (自然時効) が生
じ、この室温時効が生じた後では、前記比較的低温での
熱処理による効果が発揮しにくくなる。Further, in order to suppress room temperature aging, after the preliminary aging treatment, heat treatment at a relatively low temperature without any time delay.
(Artificial aging treatment) may be performed to further generate a GP zone. If there is a time delay, room temperature aging (natural aging) occurs over time even after pre-aging treatment, and after this room temperature aging occurs, the effect of the heat treatment at the relatively low temperature is exerted. It gets harder.
【0049】これらの効果を得るためには、Al合金材の
前記組成範囲において、時効処理温度を80〜120 ℃の範
囲とし、時効処理時間は必要時間、好ましくは1 〜24時
間の範囲とし、この範囲の中から、前記組成に応じて、
時効処理効果が得られる温度と時間を選択することが好
ましい。また、この時効処理後の冷却速度は、1 ℃/hr
以下であることが好ましい。時効処理温度が80℃未満で
は、また、保持時間が短過ぎると、GPゾーンを生成させ
ることができない。このため、室温時効抑制効果や低温
時効硬化能が得られない。一方、120 ℃を越える温度で
は通常の時効処理と大差なくなり、β" 相も析出して時
効が進み過ぎ、強度が高くなりすぎる。この点は、時効
処理の保持時間が長過ぎても同じである。なお、前記予
備時効処理温度を、後述する時効処理並に高めとし、時
効処理と合わせた乃至連続した熱処理としても良い。In order to obtain these effects, in the above composition range of the Al alloy material, the aging treatment temperature is in the range of 80 to 120 ° C., and the aging treatment time is the necessary time, preferably in the range of 1 to 24 hours, From this range, depending on the composition,
It is preferable to select the temperature and time at which the aging treatment effect is obtained. The cooling rate after this aging treatment is 1 ° C / hr.
The following is preferable. If the aging temperature is less than 80 ° C and the holding time is too short, GP zone cannot be generated. Therefore, the room temperature aging suppression effect and the low temperature age hardening ability cannot be obtained. On the other hand, at temperatures above 120 ° C, there is not much difference from normal aging treatment, β "phase also precipitates, aging proceeds too much, and strength becomes too high. This is the same even if the holding time of aging treatment is too long. The pre-aging treatment temperature may be set to be as high as the aging treatment described below, and heat treatment may be combined with or continuous with the aging treatment.
【0050】この他、用途や必要特性に応じて、更に高
温の時効処理や安定化処理を行い、より高強度化などを
図ることなども勿論可能である。In addition, it is of course possible to further increase the strength by performing aging treatment or stabilization treatment at a higher temperature depending on the use and the required characteristics.
【0051】次に、本発明Al合金板の化学成分組成の実
施形態につき、以下に説明する。本発明Al合金板の基本
組成は、上記伸びや組織などの規定、また諸特性を確保
するために、Al-Mg-Si系(6000 系)Al 合金とする。Al-M
g-Si系(6000 系)Al 合金の範囲でなければ、本発明で規
定する上記伸びや組織などにならず、また、諸特性が発
揮されない。Next, an embodiment of the chemical composition of the Al alloy sheet of the present invention will be described below. The basic composition of the Al alloy sheet of the present invention is an Al-Mg-Si-based (6000-based) Al alloy in order to ensure the above-mentioned elongation, microstructure, and other characteristics and various properties. Al-M
Unless it is in the range of g-Si (6000 series) Al alloy, the above-mentioned elongation and structure defined in the present invention are not obtained, and various properties are not exhibited.
【0052】また、上記伸びや組織などの規定および板
としての必要諸特性を確保するために、Si:0.4〜1.3%、
Mg:0.2〜1.2%、Mn:0.01 〜0.65% 、Cu:0.001〜1.0%を含
み、かつSi/Mg が質量比で1 以上とした過剰Si型のAl-M
g-Si系Al合金とすることが好ましい。そして、上記組織
の規定や諸特性を確保するために、より厳密には、前記
規定各成分以外の残部を、Alおよび不可避的不純物とす
ることが好ましい。なお、本発明での化学成分組成の%
表示は、前記請求項の% 表示も含めて、全て質量% の意
味である。Further, in order to secure the above-mentioned regulation such as elongation and structure and various necessary characteristics as a plate, Si: 0.4 to 1.3%,
Excess Si-type Al-M containing Mg: 0.2 to 1.2%, Mn: 0.01 to 0.65%, Cu: 0.001 to 1.0%, and Si / Mg of 1 or more by mass ratio.
It is preferable to use a g-Si-based Al alloy. In order to ensure the regulation and various characteristics of the above-mentioned structure, more strictly, it is preferable that the balance other than the prescribed components is Al and inevitable impurities. Incidentally,% of the chemical composition of the present invention
All the indications mean the mass% including the% indication in the above claims.
【0053】上記合金元素以外の、Cr、Zr、Ti、B 、F
e、Zn、Ni、V など、その他の合金元素は、基本的には
不純物元素である。しかし、リサイクルの観点から、溶
解材として、高純度Al地金だけではなく、6000系合金や
その他のAl合金スクラップ材、低純度Al地金などを溶解
原料として使用して、本発明Al合金組成を溶製する場合
には、これら他の合金元素は必然的に含まれることとな
る。したがって、本発明では、目的とする本発明効果を
阻害しない範囲で、これら他の合金元素が含有されるこ
とを許容する。Other than the above alloying elements, Cr, Zr, Ti, B, F
Other alloy elements such as e, Zn, Ni and V are basically impurity elements. However, from the viewpoint of recycling, as a melting material, not only high-purity Al ingots, but also 6000 series alloys and other Al alloy scrap materials, low-purity Al ingots, etc. are used as melting raw materials, In the case of smelting, these other alloying elements are inevitably included. Therefore, the present invention permits the inclusion of these other alloying elements within a range that does not impair the intended effect of the present invention.
【0054】各元素の好ましい含有範囲と意義、あるい
は許容量について以下に説明する。
Si:0.4〜1.3%。
Siは、固溶強化と、塗装焼き付け処理などの、前記低温
短時間での人工時効処理時に、MgとともにGPゾーンなど
の化合物相を形成して、時効硬化能を発揮し、パネルと
して170MPa以上の必要強度を得るための必須の元素であ
る。したがって、本発明過剰Si型6000系Al合金板にあっ
て、プレス成形性、ヘム加工性などの諸特性を兼備させ
るための最重要元素である。The preferable range and meaning of each element, or the permissible amount will be described below. Si: 0.4 to 1.3%. Si is a solid solution strengthener and forms a compound phase such as GP zone with Mg during artificial aging treatment at a low temperature and a short time, such as paint baking treatment, and exhibits age hardening ability, and a panel with 170 MPa or more as a panel. It is an essential element for obtaining the required strength. Therefore, in the excess Si type 6000 series Al alloy plate of the present invention, it is the most important element to combine various characteristics such as press formability and hemmability.
【0055】また、低温短時間での人工時効処理時 (パ
ネルへの成形後の塗装焼き付け処理、評価試験としては
2%ストレッチ付与後160 ℃×20分の低温時効処理) 時の
耐力を170MPa以上という、優れた低温時効硬化能を発揮
させるためにも、Si/Mg を質量比で1.0 以上とし、Siを
Mgに対し過剰に含有させた過剰Si型6000系Al合金組成と
することが好ましい。Further, at the time of artificial aging treatment at a low temperature for a short time (coating baking treatment after molding on a panel, as an evaluation test,
In order to exert an excellent low temperature age hardening ability of 170 MPa or more at the time of low temperature aging treatment of 160 ° C × 20 minutes after applying 2% stretch, Si / Mg is set to 1.0 or more by mass ratio and Si is
It is preferable to use an excessive Si type 6000 series Al alloy composition that is contained in excess of Mg.
【0056】Si量が0.4%未満では、前記時効硬化能、更
には、各用途に要求される、プレス成形性、ヘム加工性
などの諸特性を兼備することができない。一方、Siが1.
3%を越えて含有されると、特にヘム加工性や曲げ加工性
が著しく阻害される。更に、溶接性を著しく阻害する。
したがって、Siは0.4 〜1.3%の範囲とするのが好まし
い。なお、アウタパネルでは、ヘム加工性が特に重視さ
れるため、プレス成形性などの他の特性を低下させず
に、フラットヘム加工性をより向上させるために、Si含
有量を0.6 〜1.2%と、より低めの範囲とすることが好ま
しい。When the amount of Si is less than 0.4%, it is impossible to combine the above-mentioned age hardening ability and various characteristics required for each application such as press formability and hemmability. On the other hand, Si is 1.
If the content exceeds 3%, heme workability and bending workability are significantly impaired. Furthermore, the weldability is significantly impaired.
Therefore, Si is preferably in the range of 0.4 to 1.3%. In the outer panel, since heme workability is particularly important, in order to further improve flat heme workability without deteriorating other properties such as press formability, the Si content is 0.6 to 1.2%, A lower range is preferable.
【0057】Mg:0.2〜1.2%。
Mgは、固溶強化と、塗装焼き付け処理などの前記人工時
効処理時に、SiとともにGPゾーンなどの化合物相を形成
して、時効硬化能を発揮し、パネルとしての170MPa以上
の必要強度を得るための必須の元素である。Mg: 0.2-1.2%. In order to obtain the necessary strength of 170 MPa or more as a panel, Mg forms a compound phase such as GP zone together with Si during solid solution strengthening and artificial aging treatment such as paint baking treatment, and exhibits age hardening ability. Is an essential element of.
【0058】Mgの0.2%未満 (質量% 、以下同じ) の含有
では、絶対量が不足するため、人工時効処理時に前記化
合物相を形成できず、時効硬化能を発揮できない。この
ためパネルとして必要な前記必要強度が得られない。When the content of Mg is less than 0.2% (mass%, the same applies hereinafter), the absolute amount is insufficient, so that the compound phase cannot be formed during the artificial aging treatment and the age hardening ability cannot be exhibited. Therefore, the required strength required for the panel cannot be obtained.
【0059】一方、Mgが1.2%を越えて含有されると、プ
レス成形性や曲げ加工性 (ヘム加工性) 等の成形性が著
しく阻害される。したがって、Mgの含有量は、0.2 〜1.
2%の範囲で、かつSi/Mg が1.0 以上となるような量とす
る。また、フラットヘム加工性をより向上させるため
に、Si含有量を前記0.6 〜1.0%のより低めの範囲とする
場合には、これに対応して過剰Si型6000系Al合金組成と
するために、Mg含有量も0.2 〜0.8%と低めの範囲とする
ことが好ましい。On the other hand, when the content of Mg exceeds 1.2%, the formability such as press formability and bending workability (hem workability) is significantly impaired. Therefore, the content of Mg is 0.2-1.
The amount is within the range of 2% and the Si / Mg is 1.0 or more. Further, in order to further improve the flat heme workability, when the Si content is set to a lower range of 0.6 to 1.0%, in order to correspond to this, in order to obtain an excess Si type 6000 series Al alloy composition The Mg content is preferably in the lower range of 0.2 to 0.8%.
【0060】Cu:0.001〜1.0%
Cuは、本発明の比較的低温短時間の人工時効処理の条件
で、Al合金材組織の結晶粒内へのGPゾーンなどの化合物
相の析出を促進させる効果がある。また、時効処理状態
で固溶したCuは成形性を向上させる効果もある。Cu含有
量が0.001%未満ではこの効果がない。一方、1.0%を越え
ると、耐応力腐食割れ性や、塗装後の耐蝕性の内の耐糸
さび性、また溶接性を著しく劣化させる。このため、耐
食性が重視される構造材用途などの場合には0.8%以下、
自動車外板用などのパネル用途などの場合には、耐糸さ
び性の発現が顕著となる0.1%以下の量とすることが好ま
しい。Cu: 0.001 to 1.0% Cu has the effect of promoting the precipitation of a compound phase such as GP zone in the crystal grains of the Al alloy material structure under the conditions of artificial aging treatment at a relatively low temperature and a short time according to the present invention. There is. Further, Cu solid-dissolved in the aging treatment state also has an effect of improving formability. This effect does not occur when the Cu content is less than 0.001%. On the other hand, if it exceeds 1.0%, the stress corrosion cracking resistance, the thread rust resistance of the corrosion resistance after coating, and the weldability are significantly deteriorated. Therefore, in the case of structural material applications where corrosion resistance is important, 0.8% or less,
In the case of panel applications such as automobile outer panels, the amount is preferably 0.1% or less at which the expression of yarn rust resistance becomes remarkable.
【0061】Mn:0.01 〜0.65%
Mnには、均質化熱処理時に分散粒子 (分散相) を生成
し、これらの分散粒子に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効果
がある。前記した通り、本発明Al合金板のプレス成形性
やヘム加工性はAl合金組織の結晶粒が微細なほど向上す
る。この点、Mn含有量が0.01% 未満ではこれらの効果が
無い。Mn: 0.01 to 0.65% Mn produces dispersed particles (dispersed phase) during the homogenizing heat treatment, and these dispersed particles have an effect of hindering the movement of grain boundaries after recrystallization. It has the effect of obtaining grains. As described above, the press formability and hemmability of the Al alloy sheet of the present invention are improved as the crystal grains of the Al alloy structure are finer. In this respect, if the Mn content is less than 0.01%, these effects are not obtained.
【0062】一方、Mn含有量が多くなった場合、溶解、
鋳造時に粗大なAl-Fe-Si-(Mn、Cr、Zr) 系の金属間化合
物や晶析出物を生成しやすく、破壊の起点となり易いた
め、Al合金板の機械的性質を低下させる原因となる。ま
た、特に、前記複雑形状や薄肉化、あるいはインナパネ
ル端部とアウタパネル縁曲部内面との間の隙間の存在な
どによって、加工条件が厳しくなったフラットヘム加工
では、Mn含有量が0.25% を越えた場合、ヘム加工性が低
下する。このため、Mnは0.01〜0.65% の範囲とし、加工
条件が厳しくなったフラットヘム加工では、より好まし
くは0.01〜0.25% の範囲とする。On the other hand, when the Mn content increases, dissolution,
Coarse Al-Fe-Si- (Mn, Cr, Zr) -based intermetallic compounds and crystalline precipitates are easily generated during casting, which easily causes the starting point of fracture. Become. In addition, especially in flat hem processing where the processing conditions became strict due to the complicated shape and thinning, or the presence of a gap between the inner panel edge and the inner surface of the curved edge of the outer panel, the Mn content was 0.25%. If it exceeds the limit, the processability of the hem decreases. Therefore, Mn is set in the range of 0.01 to 0.65%, and more preferably in the range of 0.01 to 0.25% in the flat hem processing in which the processing conditions are severe.
【0063】Cr 、Zr。
これらCr、Zrの遷移元素には、Mnと同様、均質化熱処理
時に分散粒子 (分散相) を生成し、微細な結晶粒を得る
ことができる効果がある。しかし、Cr、Zrも、0.15% を
越える含有では、前記加工条件が厳しくなったフラット
ヘム加工ではヘム加工性が低下する。したがって、Cr、
Zrの含有量も、0.20% 以下に規制することが好ましい。Cr, Zr. Similar to Mn, these transition elements of Cr and Zr have an effect that dispersed particles (dispersed phase) are generated during homogenization heat treatment, and fine crystal grains can be obtained. However, when Cr and Zr also exceed 0.15%, the hem workability is deteriorated in the flat hem processing in which the above-mentioned processing conditions are severe. Therefore Cr,
The Zr content is also preferably regulated to 0.20% or less.
【0064】Ti 、B 。
Ti、B は、Ti:0.1% 、B:300ppmを各々越えて含有する
と、粗大な晶出物を形成し、成形性を低下させる。但
し、Ti、B には微量の含有で、鋳塊の結晶粒を微細化
し、プレス成形性を向上させる効果もある。したがっ
て、Ti:0.1% 以下、B:300ppm以下までの含有は許容す
る。Ti, B. If Ti and B are contained in amounts exceeding Ti: 0.1% and B: 300 ppm, respectively, coarse crystallized substances are formed and formability is deteriorated. However, if Ti and B are contained in a small amount, they also have the effect of refining the crystal grains of the ingot and improving the press formability. Therefore, Ti: 0.1% or less and B: 300ppm or less are allowed.
【0065】Fe。
溶解原料から混入して、不純物として含まれるFeは、Al
7Cu2Fe、Al12(Fe,Mn)3Cu2 、(Fe,Mn)Al6などの晶出物を
生成する。これらの晶出物は再結晶粒の核となり、Feが
0.08% 以上含まれた場合に、結晶粒の粗大化を阻止し
て、結晶粒を50μm 以下の微細粒とする役割を果たす。
しかし、一方で、これらの晶出物は、破壊靱性および疲
労特性、更には、前記加工条件が厳しくなったフラット
ヘム加工性およびプレス成形性を著しく劣化させる。こ
れらの劣化特性は、Feの含有量が0.50% を越えると顕著
になる。このため、含有させる場合のFeの含有量は、0.
08〜0.50% とすることが好ましい。Fe. Fe contained as an impurity by mixing from the melting raw material is Al
Crystallized substances such as 7 Cu 2 Fe, Al 12 (Fe, Mn) 3 Cu 2 and (Fe, Mn) Al 6 are formed. These crystallized substances become nuclei of recrystallized grains and Fe
When it is contained in an amount of 0.08% or more, it serves to prevent coarsening of the crystal grains and make the crystal grains fine particles of 50 μm or less.
However, on the other hand, these crystallized substances significantly deteriorate the fracture toughness and fatigue properties, and further the flat heme processability and press formability under severer processing conditions. These deterioration characteristics become remarkable when the Fe content exceeds 0.50%. Therefore, the content of Fe when it is contained is 0.
It is preferably set to 08 to 0.50%.
【0066】Zn。
Znは0.5%を越えて含有されると、耐蝕性が顕著に低下す
る。したがって、Znの含有量は好ましくは0.5%以下とす
ることが好ましい。Zn. If Zn is contained in excess of 0.5%, the corrosion resistance is significantly reduced. Therefore, the Zn content is preferably 0.5% or less.
【0067】(成形加工)本発明が対象とするヘム加工
は、特にフラットヘム加工を意図している。即ち、アウ
タパネルの縁をポンチなどの工具により90°に近い角度
まで折り曲げるダウンフランジ工程、アウタパネルの縁
を更に約135 °まで内側に折り曲げるプリヘム工程を経
て、インナパネル端部をアウタパネルの折り曲げ部内に
収容 (挿入) し、アウタパネルの縁を工具により更に18
0 °の角度まで内側に折り曲げてフラットヘムが形成さ
れる。このフラットヘムでは、インナパネルと、アウタ
パネルの180 度折り曲げ部とが接合、密着され、フラッ
トな曲げ部形状を有する。(Molding) The hem processing targeted by the present invention is intended to be a flat hem processing. That is, the inner panel edge is stored in the bent part of the outer panel through a down-flange process that bends the outer panel edge to an angle close to 90 ° with a tool such as a punch, and a prehem process that bends the outer panel edge further inward to approximately 135 °. (Insert), and then the edge of the outer panel
The flat hem is formed by bending inward to an angle of 0 °. In this flat hem, the inner panel and the 180-degree bent portion of the outer panel are joined and adhered to each other to have a flat bent portion shape.
【0068】しかし、本発明は厳しい条件であるフラッ
トヘム加工性に優れるので、それよりも一段緩い条件で
ある、前記折り曲げ部が円弧状に膨らんだロープ状の断
面形状を有しいるロープヘムなどの加工性にも当然優れ
る。また、加工 (変形) の機構が共通する、前記他のハ
ット型曲げ加工や90度曲げ加工などの曲げ加工性や、あ
るいは、一般的にV 曲げ、U 曲げ、端曲げ、波曲げ、引
張曲げなどと称される曲げ加工性にも優れる。したがっ
て、本発明は、他のロープヘムなどのヘム加工も対象と
し、ヘム加工以外の曲げ加工も対象とする。However, since the present invention is excellent in workability in flat hem, which is a severe condition, it is a condition looser than that, such as a rope hem having a rope-shaped cross section in which the bent portion bulges in an arc shape. Naturally also excellent in workability. In addition, bending workability such as hat-type bending work and 90-degree bending work other than the above, which has a common processing (deformation) mechanism, or generally, V bending, U bending, end bending, wave bending, tensile bending Also has excellent bending workability. Therefore, the present invention is also applicable to hem processing such as other rope hem, and also to bending processing other than hem processing.
【0069】また、ヘム加工は、前記した、ダウンフラ
ンジ工程、プリヘム工程、フラットヘム乃至ロープヘム
工程により行われる通常のヘム加工だけでなく、最終的
にヘムが形成されるものであれば、ローラーヘムなど、
工程や工程条件が異なるものもヘム加工として対象とす
るし、適用可能である。The hem processing is not limited to the normal hem processing performed by the down-flange process, the pre-hem process, the flat hem or the rope hem process described above, and if the hem is finally formed, it is a roller hem process. Such,
Those having different processes and process conditions are also applicable and applicable as hemming.
【0070】なお、フラットヘムなどのヘム加工が、本
発明Al合金板の4 周囲に対して全て行われるか、選択さ
れる辺 (側縁部) のみに対して行われか、また、ヘム加
工されるアウタパネルの端部形状が直線形状か、円弧形
状やあるいは角部を有するような複雑形状かは、アウタ
パネルなどの部材設計に応じて、適宜選択される。It should be noted that the hem processing such as the flat hem is carried out on all four peripheries of the Al alloy sheet of the present invention, or only on the selected side (side edge portion), and the hem processing is carried out. Whether the end shape of the outer panel to be formed is a linear shape, an arc shape, or a complicated shape having a corner is appropriately selected according to the member design of the outer panel and the like.
【0071】本発明は、また、ヘム加工性と同時に、上
記張出などのプレス成形を対象とする。そして、プレス
成形の中でも、特に、アウタパネルなどにおける、前記
した形状が大型化、複雑化した際の張出成形を対象とす
る。ただ、これらの張出成形性に優れることは、加工条
件が比較的緩やかな、他の絞りなどの成形性に優れるこ
とを意味する。したがって、本発明Al合金板は、特に張
出成形、また張出成形で代表できる他のプレス成形をも
対象とする。The present invention is also directed to press forming such as the above-mentioned overhanging, as well as hemmability. Further, among the press forming, particularly, the bulging forming when the above-mentioned shape becomes large and complicated in the outer panel or the like is targeted. However, the excellent bulging formability means that the processability is relatively mild and the formability of other drawing is excellent. Therefore, the Al alloy sheet of the present invention is particularly intended for stretch forming, and other press forming represented by stretch forming.
【0072】[0072]
【実施例】次に、本発明の実施例を説明する。表1 に示
す過剰Si型の6000系のAl合金板 (熱間圧延板) につい
て、異方性を持つ集合組織を得るために、表2 に示すよ
うに、前半の冷間圧延の圧下率、この冷間圧延後の中間
焼鈍の焼鈍温度 (焼鈍時間は全て3 時間とした) 、中間
焼鈍後の後半の冷間圧延の圧下率、を各々種々変えて厚
さ1.0mm のAl合金冷延板を作成した。EXAMPLES Next, examples of the present invention will be described. Regarding the excess Si type 6000 series Al alloy plate (hot rolled plate) shown in Table 1, in order to obtain a texture with anisotropy, as shown in Table 2, the reduction ratio of the cold rolling in the first half, The Al alloy cold-rolled sheet with a thickness of 1.0 mm was variously changed by varying the annealing temperature of the intermediate annealing after the cold rolling (the annealing time was all 3 hours) and the reduction rate of the cold rolling in the latter half after the intermediate annealing. It was created.
【0073】なお、熱間圧延までのAl合金板の作製は、
上記冷間圧延の圧下率を変化させるための熱間圧延板の
板厚を除き、ほぼ同じ条件で行った。即ち、表1 に示す
組成範囲の400mm 厚の鋳塊を、DC鋳造法により溶製後、
540 ℃×4 時間の均質化熱処理を施し、終了温度300 ℃
で厚さ2.3 〜8mmtまで板厚を種々変えて熱間圧延した。The production of the Al alloy plate until hot rolling is
The same conditions were used except for the thickness of the hot rolled plate for changing the reduction ratio of the cold rolling. That is, a 400 mm thick ingot having the composition range shown in Table 1 was melted by the DC casting method,
540 ℃ × 4 hours homogenized heat treatment, finish temperature 300 ℃
Was hot-rolled with various thicknesses ranging from 2.3 to 8 mmt.
【0074】更に、上記冷延板は以下の条件で調質処理
した。先ず、上記冷延板を570 ℃に保持した空気炉に投
入し、各試験片が550 ℃の溶体化処理温度に到達した時
点で(保持時間 0秒) 、80℃の温水に焼き入れする処理
を行った。前記焼入れ処理の際の冷却速度は200 ℃/ 秒
とし、焼入れ終了温度 (焼入れ温度) は共通して80℃と
し、焼入れ後にこの温度で2 時間保持する予備時効処理
(保持後は冷却速度0.6 ℃/hr で徐冷) を行った。Further, the cold-rolled sheet was heat-treated under the following conditions. First, the cold-rolled sheet was placed in an air furnace maintained at 570 ° C, and when each test piece reached the solution treatment temperature of 550 ° C (holding time 0 seconds), it was quenched in hot water of 80 ° C. I went. The cooling rate at the time of the quenching treatment was 200 ° C / sec, the quenching end temperature (quenching temperature) was 80 ° C in common, and the pre-aging treatment was held at this temperature for 2 hours after quenching.
(After holding, it was gradually cooled at a cooling rate of 0.6 ° C / hr).
【0075】これら調質処理後のAl合金板から試験用の
幅500mm ×長さ500mm の供試板 (ブランク) を複数枚切
り出し、調質処理後に十分室温時効したAl合金板がプレ
ス成形およびヘム加工されることを想定して、前記調質
処理後 4カ月間 (120 日間)の室温時効後の、各供試板
の平均結晶粒径、圧延方向に平行なAS耐力 (σ0.2)、Al
合金板表面における{200 }面の積分強度の割合と、
{200 }面と{400 }面との合計積分強度の割合を前記
したX 線回折測定方法により測定した。これらの結果を
表2 に示す。A plurality of test plates (blanks) each having a width of 500 mm and a length of 500 mm for testing were cut out from the Al alloy plate after the heat treatment, and the Al alloy plate sufficiently aged at room temperature after the heat treatment was press-formed and hem. Assuming that it is processed, the average grain size of each test plate, AS proof stress (σ 0.2 ) parallel to the rolling direction, and Al after 4 months (120 days) after tempering treatment at room temperature
The ratio of the integrated intensity of the {200} plane on the alloy plate surface,
The ratio of the total integrated intensity of the {200} plane and the {400} plane was measured by the above-mentioned X-ray diffraction measurement method. The results are shown in Table 2.
【0076】なお、耐力測定のための引張試験はJIS Z
2201にしたがって行うとともに、試験片形状はJIS 5 号
試験片で行った。また、クロスヘッド速度は5mm/分で、
試験片が破断するまで一定の速度で行った。The tensile test for measuring the proof stress is JIS Z
According to 2201, the test piece shape was JIS 5 test piece. Also, the crosshead speed is 5 mm / min,
The test was performed at a constant speed until the test piece broke.
【0077】また、前記室温時効した供試板を、自動車
パネルとしてプレス成形やヘム加工されることを模擬し
て、成形試験した。より具体的には、張出成形試験、張
出成形後のフラットヘム加工試験を行い、成形性を評価
した。これらの結果を表3 に示す。The test plate aged at room temperature was subjected to a forming test by simulating press forming and hemming as an automobile panel. More specifically, an extension molding test and a flat hem processing test after the extension molding were performed to evaluate the formability. The results are shown in Table 3.
【0078】張出成形試験の条件は、前記供試板 (ブラ
ンク) を、中央部に一辺が300mm で高さが30mmと高い角
筒状の張出部と、この張出部の四周囲に平坦なフランジ
部 (幅30mm) を有するハット型のパネルに、メカプレス
により、ビード付き金型を用いて張出成形した。The conditions for the bulging molding test were as follows: the test plate (blank) was a rectangular tubular bulging part with a side of 300 mm and a height of 30 mm in the central part, and four surrounding parts of the bulging part. A hat-shaped panel having a flat flange portion (width 30 mm) was stretch-molded by a mechanical press using a beaded mold.
【0079】張出成形試験は、しわ押さえ力は49kN、潤
滑油は一般防錆油、成形速度は20mm/ 分の同じ条件で3
回行い、3 回とも成形ハット型パネルの張出部角部など
に割れがなく正常に成形できた例を〇、3 回とも全て割
れが生じて成形できなかったものを×として評価した。In the bulging test, the wrinkle holding force was 49 kN, the lubricating oil was general rust preventive oil, and the molding speed was 3 mm under the same conditions of 20 mm / min.
Molding was carried out three times, and in all three cases, there were no cracks in the overhanging corners of the hat-shaped panel and normal molding was possible, and in all three cases, cracking occurred and molding could not be carried out.
【0080】成形品のリジングマークなどの表面性状の
評価は、上記張出成形試験の成形品を洗浄後、同一条件
でリン酸亜鉛処理、塗装および焼き付け処理を行った後
の成形品表面の外観を評価し、リジングマークや肌荒れ
の発生状況により行った。前記3 回(3個) の成形品表面
に、3 個とも全てリジングマークや肌荒れが生じていな
いものを〇、1 個でもリジングマークや肌荒れが生じて
いるものを×と評価した。The surface properties such as the ridging mark of the molded product were evaluated by washing the molded product of the above-mentioned bulging test and then applying the zinc phosphate treatment, coating and baking treatment under the same conditions to the appearance of the surface of the molded product. The evaluation was performed according to the occurrence status of ridging marks and rough skin. On all three surfaces (three pieces) of the surface of the molded article, all three pieces without ridging marks or rough skin were evaluated as ◯, and even one piece with ridging marks or rough surface was evaluated as x.
【0081】なお、この際のリン酸亜鉛処理は、リン酸
チタンのコロイド分散液による処理を行い、次いでフッ
素を50ppm の低濃度含むリン酸亜鉛浴に浸漬してリン酸
亜鉛皮膜を成形材表面に形成した。その後の塗装処理
は、カチオン電着塗装を行った後に、170 ℃×20分の焼
き付けを行う条件とした。In this case, the zinc phosphate treatment is performed by a colloidal dispersion of titanium phosphate, and then immersed in a zinc phosphate bath containing fluorine at a low concentration of 50 ppm to form a zinc phosphate coating on the surface of the molding material. Formed. The subsequent coating treatment was carried out under the condition of performing cationic electrodeposition coating and then baking at 170 ° C. for 20 minutes.
【0082】次に、フラットヘム加工試験は以下の通り
とした。前記張出成形されたAl合金パネルを、アウター
パネルとしてヘム加工されることを模擬して、パネルの
前記平坦なフランジ部の内、圧延方向と平行なフランジ
部の端部全面 (幅130mm)を以下の条件でフラットヘム加
工した。Next, the flat hem processing test was conducted as follows. The bulging-formed Al alloy panel, simulating that it is hem processed as an outer panel, of the flat flange portion of the panel, the entire end portion of the flange portion parallel to the rolling direction (width 130 mm) Flat hem processing was performed under the following conditions.
【0083】より具体的には、まず、Al合金パネルのフ
ラットヘム加工代 (ヘム加工後のパネルの内側に折り曲
げられた端部から折り曲げ部の端部までの距離) を12mm
として、ダウンフランジ工程を模擬し、Al合金パネルの
縁を90度の角度となるまで折り曲げた。この際、Al合金
パネルの90°曲げ半径は0.8 とした。次に、プリヘム工
程模擬して、Al合金パネルの縁を更に135 °の角度まで
内側に折り曲げた。More specifically, first, the flat hemming allowance of the Al alloy panel (distance from the end bent inside the panel after the hemming to the end of the bent part) is 12 mm.
As a result, the down flange process was simulated, and the edge of the Al alloy panel was bent to an angle of 90 degrees. At this time, the 90 ° bending radius of the Al alloy panel was 0.8. Next, by simulating the prehem process, the edge of the Al alloy panel was further bent inward to an angle of 135 °.
【0084】その後、厳しいフラットヘム加工条件を模
擬して、敢えてインナパネルを前記Al合金パネルの折り
曲げ部に挿入せずに、折り曲げ部を内側に180 度折り曲
げ、パネル面に密着させるフラット曲げ加工を行った。
なお、ヘム加工方向は、元のAl合金板の圧延方向と一致
するようにした。After that, simulating the severe flat hem processing conditions, without inserting the inner panel into the bent portion of the Al alloy panel, the bent portion is bent 180 degrees inward, and the flat bending processing is performed to bring it into close contact with the panel surface. went.
The hemming direction was made to coincide with the rolling direction of the original Al alloy plate.
【0085】そして、このフラットヘムの縁曲部の、肌
荒れ、微小な割れ、大きな割れの発生などの表面状態を
目視観察した。評価は、1;肌荒れや微小な割れも無く良
好、2;肌荒れが発生しているものの、微小なものを含め
た割れはない、3;微小な割れが発生、4;大きな割れが発
生、5;大きな割れが複数乃至多数発生、の5 段階の評価
(5段階の各中間の評価を含む) をした。この評価とし
て、ヘム加工性が良好 (使用可) と判断されるのは1 〜
2 段階までで、3 段階以上はヘム加工性が劣る (使用不
可) と判断される。Then, the surface condition such as rough skin, fine cracks, and large cracks was visually observed at the curved edge of the flat hem. The evaluation is 1; good with no rough skin or fine cracks, 2; no rough cracks, including small ones, 3; fine cracks, 4; large cracks, 5 ; Evaluation in 5 levels, with multiple or multiple major cracks
(Including the evaluation of each of the five stages). For this evaluation, it is judged that the hemmability is good (usable) from 1 to
It is judged that the hem processability is inferior (unusable) for 3 or more steps up to 2 steps.
【0086】更に、人工時効処理能を調査するため、前
記プレス成形されたAl合金パネルから供試板を採取し
て、160 ℃×20分の低温短時間の人工時効硬化処理し、
処理後の各供試板の (元のAl合金板の) 圧延方向に平行
な(L方向の) 耐力 (ABσ0.2)を測定した。これらの結果
を表3 に示す。Further, in order to investigate the artificial aging treatment ability, a sample plate was taken from the press-formed Al alloy panel and subjected to artificial aging hardening treatment at a low temperature for a short time of 160 ° C. × 20 minutes,
The proof stress (AB σ 0.2 ) parallel to the rolling direction (of the original Al alloy plate) (AB σ 0.2 ) of each test plate after the treatment was measured. The results are shown in Table 3.
【0087】表2 、3 から明らかな通り、前半の冷間圧
延の圧下率、中間焼鈍温度、後半の冷間圧延の圧下率な
どの、本発明の製造条件を満足する発明例1 〜6 は、平
均結晶粒が50μm 以下と微細であり、前記 4カ月間 (12
0 日間) の室温時効後でも、張出成形後もリジングマー
クや肌荒れが生じておらず、成形品の表面性状評価は○
で著しく優れている。また、Al合金板表面における{20
0 }面の積分強度の割合が70% 以上、{200 }面と{40
0 }面との合計積分強度の割合が80% 以上であり、キュ
ーブ方位を有する結晶粒の割合が高い異方性を有する集
合組織であり、フラットヘム加工性に優れている。更
に、張出成形性にも優れ、AB耐力が200MPa以上と高く時
効硬化性などの諸特性にも優れている。As is clear from Tables 2 and 3, Invention Examples 1 to 6 satisfying the manufacturing conditions of the present invention, such as the first half cold rolling reduction, the intermediate annealing temperature, and the second half cold rolling reduction, were prepared. , The average grain size is as fine as 50 μm or less, and
After aging at room temperature for 0 days), neither ridging marks nor rough skin was observed after stretch molding, and the surface quality of the molded product was evaluated as ○.
Is remarkably excellent in. In addition, {20 on the surface of the Al alloy plate
The ratio of the integrated intensity of the 0} plane is 70% or more, and the {200} plane and the {40} plane
The ratio of the total integrated intensity with respect to the (0) plane is 80% or more, the ratio of the crystal grains having the cube orientation is a highly anisotropic texture, and the flat heme processability is excellent. Furthermore, it has excellent stretchability, AB proof stress of 200 MPa or more, and various properties such as age hardening.
【0088】前記フラットヘム加工性の試験条件と評価
は、自動車アウタパネルなどの実際の厳しい加工条件で
のフラットヘム加工性の評価につながるものである。し
たがって、発明例1 〜6 は、実際のフラットヘムなどの
ヘム加工でも、十分加工できることを示している。The test conditions and evaluation of the flat hem processability lead to the evaluation of the flat hem processability under actual severe process conditions such as the outer panel of an automobile. Therefore, Invention Examples 1 to 6 show that even hemming such as an actual flat hem can be sufficiently processed.
【0089】また、前記張出成形の試験条件と評価は、
自動車アウタパネルなどの実際の厳しい加工条件での張
出成形の評価につながるものである。したがって、発明
例1〜6 は、実際の張出成形や絞り成形などのプレス成
形で、張出高さや張出面積などが大型化しても、張出成
形性が優れ、十分加工できることを示している。The test conditions and evaluation of the above-mentioned bulge molding are as follows.
This leads to evaluation of stretch forming under actual severe processing conditions such as automobile outer panels. Therefore, Invention Examples 1 to 6 show that in actual press forming such as bulging and drawing, even if the bulging height and bulging area increase, the bulging formability is excellent and sufficient processing is possible. There is.
【0090】一方、前半の冷延における圧下率が低す
ぎ、後半の冷延における圧下率が高すぎる比較例7 、前
半の冷延における圧下率が高すぎ、後半の冷延における
圧下率が低すぎる比較例8 、中間焼鈍温度が高すぎる比
較例9 、逆に中間焼鈍温度が低すぎる比較例10、前半の
冷延における圧下率が高めで、後半の冷延における圧下
率が低すぎる比較例11は、いずれも、平均平均結晶粒径
が50μm を越えており、張出成形後にリジングマークや
肌荒れが生じて、成形品の表面性状が著しく劣ってい
る。On the other hand, the rolling reduction in the first half cold rolling was too low, and the rolling reduction in the latter half cold rolling was too high. Comparative Example 7, the rolling reduction in the first half cold rolling was too high, and the rolling reduction in the second half cold rolling was too low. Comparative Example 8 too, intermediate annealing temperature is too high Comparative Example 9, intermediate annealing temperature is too low Comparative Example 10, the rolling reduction in the first half cold rolling is high, the rolling reduction in the latter half cold rolling is too low Comparative Example In Nos. 11 and 12, the average average crystal grain size exceeds 50 μm, and ridging marks and skin roughness are generated after the bulging and the surface properties of the molded product are remarkably inferior.
【0091】また、比較例7 、8 、9 、11は、張出成形
は良いものの、キューブ方位を有する結晶粒の割合が低
く、フラットヘム加工性にも劣っている。したがって、
これらの結果から、本発明製造方法における各規定の臨
界的な意義が分かる。また、これらの結果 (効果) は過
剰Si型以外のAl-Mg-Si系Al合金板にも、当てはまるもの
である。In Comparative Examples 7, 8, 9, and 11, although the stretch forming was good, the proportion of crystal grains having the cube orientation was low and the flat heme processability was also poor. Therefore,
From these results, the critical significance of each regulation in the production method of the present invention is understood. Moreover, these results (effects) are also applicable to Al-Mg-Si based Al alloy plates other than the excess Si type.
【0092】[0092]
【表1】 [Table 1]
【0093】[0093]
【表2】 [Table 2]
【0094】[0094]
【表3】 [Table 3]
【0095】[0095]
【発明の効果】本発明によれば、室温時効したとして
も、ヘム加工などの曲げ加工性に優れ、更にリジングマ
ークや肌荒れを抑制してプレス成形性にも優れた6000系
Al合金板の製造方法を提供することができる。したがっ
て、6000系Al合金板のパネル用途への拡大を図ることが
できる点で、多大な工業的な価値を有するものである。According to the present invention, the 6000 series is excellent in bending workability such as hemming even when aged at room temperature, and is excellent in press formability by suppressing ridging marks and rough skin.
A method for manufacturing an Al alloy plate can be provided. Therefore, it has a great industrial value in that the 6000 series Al alloy plate can be expanded to panel applications.
───────────────────────────────────────────────────── 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 630A 630K 630M 640 640A 681 681 682 682 683 683 685 685A 686 686A 691 691A 691B 692 692A 694 694A ─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. 7 Identification code FI theme code (reference) C22F 1/00 623 C22F 1/00 623 630 630 630A 630K 630M 640 640A 681 681 682 682 683 683 683 685 686A 686 691A 691B 692 692A 694 694A
Claims (4)
合金板を、10〜50%の圧下率で冷間圧延後、210 〜440
℃の温度で焼鈍し、更に70% 以上の圧下率で冷間圧延し
た後、溶体化および焼入れ処理し、アルミニウム合金板
の集合組織に異方性を持たせるとともに、平均結晶粒径
を50μm 以下とすることを特徴とする曲げ加工性に優れ
たアルミニウム合金板の製造方法。1. A hot rolled Al-Mg-Si based aluminum alloy sheet is cold rolled at a rolling reduction of 10 to 50%, and then 210 to 440.
After annealing at a temperature of ℃ and cold rolling at a reduction of 70% or more, solution treatment and quenching are applied to make the texture of the aluminum alloy sheet anisotropic, and the average grain size is 50 μm or less. A method for producing an aluminum alloy sheet having excellent bending workability, comprising:
3%、Mg:0.2〜1.2%、Mn:0.01 〜0.65% 、Cu:0.001〜1.0%
を含み、かつSi/Mg が質量比で1 以上であり、残部がAl
および不可避的不純物である組成からなる請求項1に記
載の曲げ加工性に優れたアルミニウム合金板の製造方
法。2. The aluminum alloy plate has a Si: 0.4-1.
3%, Mg: 0.2-1.2%, Mn: 0.01-0.65%, Cu: 0.001-1.0%
And the ratio of Si / Mg is 1 or more by mass and the balance is Al
The method for producing an aluminum alloy sheet having excellent bendability according to claim 1, wherein the aluminum alloy sheet has a composition of unavoidable impurities.
が、アルミニウム合金板に表面における{200 }面の積
分強度の割合が70% 以上であるとともに{200}面と{4
00 }面との合計積分強度の割合が80% 以上である請求
項1または2に記載の曲げ加工性に優れたアルミニウム
合金板の製造方法。3. The anisotropy of the structure of the aluminum alloy plate is such that the ratio of the integrated strength of the {200} face on the surface of the aluminum alloy plate is 70% or more and the anisotropy of the {200} face and the {4} face is
The method for producing an aluminum alloy sheet having excellent bending workability according to claim 1 or 2, wherein a ratio of the total integrated strength with respect to the {00} plane is 80% or more.
ヘム加工される請求項1乃至3のいずれか1項に記載の
曲げ加工性に優れたアルミニウム合金板の製造方法。4. The method for producing an aluminum alloy sheet having excellent bending workability according to claim 1, wherein the aluminum alloy sheet is hemmed after stretch forming.
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Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2005256053A (en) * | 2004-03-10 | 2005-09-22 | Kobe Steel Ltd | Aluminum alloy sheet having excellent bending workability and press formability |
KR100569454B1 (en) | 2004-10-12 | 2006-04-07 | 현대자동차주식회사 | Method of manufacturing al-mg-si alloy sheet |
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