JP5050577B2 - Aluminum alloy plate for forming process excellent in deep drawability and bake-proof softening property and method for producing the same - Google Patents
Aluminum alloy plate for forming process excellent in deep drawability and bake-proof softening property and method for producing the same Download PDFInfo
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Description
本発明は、家電製品や自動車の外板などの構造材に見られるように、例えば深絞り成形加工後に焼付け塗装が施されるような場合、成形加工性に優れかつ焼付け処理後に高い強度が求められる成形加工用アルミニウム合金板に関する。 As seen in structural materials such as home appliances and automobile outer plates, the present invention requires excellent formability and high strength after baking, for example, when baking coating is applied after deep drawing. The present invention relates to an aluminum alloy plate for forming.
Ａｌ−Ｍｇ系合金は、成形性に優れていることから、当該技術分野において種々の製造方法、成形性に優れた合金板、特に深絞り成形性に優れた合金板が提唱されてきた。 Since Al—Mg alloys are excellent in formability, various production methods and alloy plates excellent in formability, particularly alloy plates excellent in deep drawability have been proposed in the technical field.
成形加工用のアルミニウム合金板として、従来からＪＩＳ ５０５２合金、ＪＩＳ ５１８２合金材が使用されてきた。深絞り成形加工に適するＡｌ−Ｍｇ系合金板の製造方法としては、所定の組成の溶湯をＤＣ鋳造してスラブとし、両面面削後に均質化処理を施して、熱間圧延、中間冷間圧延、中間焼鈍、最終冷間圧延、最終焼鈍を行うことが一般的である。特許文献１では、このような一般的な製造方法を採用し、Ｍｎ、Ｃｒを添加することにより、焼鈍板の集合組織および結晶粒径を適正な範囲として、（１１０）方位集積度などを制御した深絞り成形性に優れたＡｌ−Ｍｇ系合金板が提案されている。 Conventionally, JIS 5052 alloy and JIS 5182 alloy material have been used as aluminum alloy plates for forming. As a method for producing an Al-Mg alloy sheet suitable for deep drawing, a molten metal having a predetermined composition is DC-cast to form a slab, subjected to homogenization after both-side chamfering, hot rolling, intermediate cold rolling In general, intermediate annealing, final cold rolling, and final annealing are performed. In Patent Document 1, such a general manufacturing method is adopted, and by adding Mn and Cr, the texture and crystal grain size of the annealed plate are set within an appropriate range, and the (110) orientation integration degree and the like are controlled. An Al-Mg alloy plate excellent in deep drawability has been proposed.
また、絞り比が２．０に近い食缶材等の深絞り成形において、ストレッチャー・ストレインマーク（ＳＳマーク）が発生し、プレス加工速度の増大や温度制御によるＳＳマークの防止が困難であることから、材料面からの改善が要望されていた。特許文献２では、中間圧延における加工率、中間焼鈍温度、仕上げ圧延における加工率、安定化焼鈍温度などを規定することにより、特に絞り比が２．０に近い深絞り加工においてもストレッチャー・ストレインマークの発生しないＡｌ−Ｍｇ合金板の製造方法が提案されている。 In addition, in deep drawing of food cans with a drawing ratio close to 2.0, stretcher strain marks (SS marks) are generated, and it is difficult to increase the press working speed and prevent SS marks by temperature control. Therefore, improvement from the material aspect has been demanded. In Patent Document 2, by specifying the processing rate in intermediate rolling, the intermediate annealing temperature, the processing rate in finish rolling, the stabilized annealing temperature, and the like, particularly in deep drawing with a drawing ratio close to 2.0, stretcher strain A method for producing an Al—Mg alloy plate free of marks has been proposed.
さらに、ＤＩ缶など深絞り缶の製造において、ネックの縮径率を大きくするとネック耳が生じ、しごき加工後のトリム加工において耳も除去され歩留まりが低下して製造コストが上昇するという問題があった。特許文献３では、トリム加工の際に除去される板材の量割合（耳率）を低くするため、熱間圧延の全工程にシングルミルのリバース式熱間粗圧延機を用い、熱間圧延、中間冷間圧延、中間焼鈍、最終冷間圧延などの製造条件を細かく規定した深絞り成形用アルミニウム基合金板の製造方法が開示されている。 Furthermore, in the manufacture of deep drawn cans such as DI cans, there is a problem that when the diameter reduction ratio of the neck is increased, neck ears are generated, and the ears are also removed in the trim processing after ironing, resulting in a decrease in yield and an increase in manufacturing cost. It was. In Patent Document 3, in order to reduce the amount ratio (ear ratio) of the plate material to be removed during trim processing, a single-mill reverse hot rough rolling mill is used for all the hot rolling processes, A method of manufacturing an aluminum-based alloy sheet for deep drawing, in which manufacturing conditions such as intermediate cold rolling, intermediate annealing, and final cold rolling are specified in detail, is disclosed.
一方、耐焼付け軟化性について、特許文献４では、質量％で、Ｍｇ：２〜５％、Ｆｅ：０．０５を超え１．５％以下、Ｍｎ：０．０５〜１．５％および結晶粒微細化剤を含有し、残部Ａｌおよび不可避的不純物からなり、不可避的不純物のうちＳｉ：０．２０％未満とし、Ｆｅ＋Ｍｎ＞０．３％であり、Ｆｅの固溶量が５０ｐｐｍ以上で、円相当径で１〜６μｍの金属間化合物が５０００個／ｍｍ２以上存在し、しかも再結晶粒径の平均値が２０μｍである耐焼付け軟化性に優れたアルミニウム合金板が提案されている。 On the other hand, regarding the softening resistance to seizure, in Patent Document 4, Mg: 2 to 5%, Fe: more than 0.05 and 1.5% or less, Mn: 0.05 to 1.5% and crystal grains in mass% It contains a refining agent, and consists of the balance Al and unavoidable impurities. Among unavoidable impurities, Si: less than 0.20%, Fe + Mn> 0.3%, Fe solid solution amount of 50 ppm or more, There has been proposed an aluminum alloy plate excellent in seizure softening resistance, in which an intermetallic compound having an equivalent diameter of 1 to 6 μm is present in an amount of 5000 / mm 2 or more and the average recrystallized grain size is 20 μm.
家電製品や自動車の外板などの構造材などを深絞り加工した場合に外観を綺麗に仕上げるため、焼付け塗装が施されるケースも多い。この場合、従来法で製造された所謂ＤＣ材では、深絞り加工性に優れるＡｌ−Ｍｇ合金板であっても、マトリックス中におけるＦｅ、Ｍｎ、Ｃｒなどの遷移金属元素の固溶量が低いために、焼付け塗装時の加熱によって転位の回復が起こり、成形部材の強度が低下するという問題点があった。さらに上述したように、従来法では、所定の組成の溶湯をＤＣ鋳造によりスラブを製造し、両面面削後に均質化処理を施して、熱間圧延、中間冷間圧延、中間焼鈍、最終冷間圧延、最終焼鈍を施すため、工程が複雑となり製造コストが高くなるという問題点もあった。 In many cases, a deep-drawing process is performed on structural materials such as home appliances and automobile outer panels, so that the appearance is beautifully baked. In this case, the so-called DC material manufactured by the conventional method has a low solid solution amount of transition metal elements such as Fe, Mn, and Cr in the matrix even in the case of an Al-Mg alloy plate having excellent deep drawing workability. Furthermore, there is a problem in that dislocation recovery occurs due to heating during baking coating, and the strength of the molded member is reduced. Furthermore, as described above, in the conventional method, a slab is manufactured by DC casting of a molten metal having a predetermined composition, subjected to homogenization treatment after double-side chamfering, hot rolling, intermediate cold rolling, intermediate annealing, final cold Since rolling and final annealing are performed, there is a problem that the process becomes complicated and the manufacturing cost increases.
本発明は、上記従来の問題を解決し、複雑な製造工程を必要とせずに、深絞り性と耐焼付け軟化性とを同時に高めた成形加工用アルミニウム合金板およびその製造方法を提供することを目的とする。 The present invention solves the above-mentioned conventional problems, and provides an aluminum alloy plate for forming and a method for producing the same that have improved deep drawability and anti-seizure softening properties without requiring a complicated production process. Objective.
上記目的を達成するために、本発明の成形加工用アルミニウム合金板は、質量％で、Ｍｇ：１〜５％、Ｆｅ：０．１〜１．０％、Ｔｉ：０．００５〜０．１％、Ｂ：０．０００５〜０．０１％を含み、残部Ａｌと不可避的不純物からなり、不可避的不純物のうちＳｉ：０．２０％未満とし、マトリックス中のＦｅの固溶量が５０ｐｐｍ以上であり、再結晶粒径が１２μｍ以下、限界絞り比が２．１３以上であることを特徴とする。 In order to achieve the above object, the aluminum alloy sheet for forming according to the present invention is in mass%, Mg: 1 to 5%, Fe: 0.1 to 1.0%, Ti: 0.005 to 0.1. %, B: 0.0005 to 0.01%, the balance is Al and inevitable impurities, Si is less than 0.20% among the inevitable impurities, and the solid solution amount of Fe in the matrix is 50 ppm or more. The recrystallized grain size is 12 μm or less, and the limiting drawing ratio is 2.13 or more.
上記の成形加工用アルミニウム合金板を製造する方法は、本発明によれば、質量％で、Ｍｇ：１〜５％、Ｆｅ：０．１〜１．０％、Ｔｉ：０．００５〜０．１％、Ｂ：０．０００５〜０．０１％を含み、残部Ａｌと不可避的不純物からなり、不可避的不純物のうちＳｉ：０．２０％未満とする合金組成の溶湯を双ベルト式鋳造機により連続鋳造して薄スラブとし、該薄スラブに均質化処理および中間焼鈍を施すことなく、冷間圧延を行った後に、最終焼鈍を施すことを特徴とする。 According to the present invention, the method for producing the above-described aluminum alloy sheet for forming is in mass%, Mg: 1-5%, Fe: 0.1-1.0%, Ti: 0.005-0. 1%, B: 0.0005-0.01%, the balance is Al and unavoidable impurities, Si: less than 0.20% of the unavoidable impurities of the alloy composition of molten metal by a double belt caster A continuous slab is formed into a thin slab. The thin slab is subjected to final rolling after cold rolling without being subjected to homogenization and intermediate annealing.
本発明の成形加工用アルミニウム合金板においては、再結晶粒が１２μｍ以下のサイズであり、しかも再結晶時に圧延集合組織を残存させ、（１１０）方位を得やすく、ｒ値やＬＤＲが高く深絞り性に優れたＡｌ−Ｍｇ系合金板を製造することができる。しかも、このＡｌ−Ｍｇ系合金板は、マトリックス中におけるＦｅ、Ｍｎなどの遷移金属元素の固溶量が高く、成形後の焼付け塗装時の加熱による耐力の低下が少ないため、耐焼付け軟化性にも優れている。 In the aluminum alloy sheet for forming according to the present invention, the recrystallized grains have a size of 12 μm or less, and the rolled texture remains at the time of recrystallization so that the (110) orientation can be easily obtained, and the r value and LDR are high. An Al—Mg-based alloy plate having excellent properties can be manufactured. In addition, this Al-Mg alloy plate has a high solid solution amount of transition metal elements such as Fe and Mn in the matrix, and since there is little decrease in yield strength due to heating during baking after molding, Is also excellent.
本発明の製造方法によると、双ベルト鋳造機による薄スラブ鋳造時、薄スラブ中にＡｌ-Ｆｅ、Ａｌ-（Ｆｅ・Ｍｎ）-Ｓｉ、Ａｌ-Ｃｒ系化合物などが均一かつ微細に晶出して、最終焼鈍時に再結晶粒の核となり、同時に結晶粒界の移動を妨げるピン止め効果を発揮するため、再結晶粒径が１２μｍ以下と微細になる。また、母相Ａｌ中に過飽和に固溶したＦｅ、Ｍｎなど遷移金属元素が、Ｍｇとともに固溶体強化元素となり、再結晶の際に圧延集合組織の転位やセル境界の移動を止め、そこに存在する圧延集合組織を残存させる。この結果、（１１０）方位が得られ、ｒ値やＬＤＲが高く深絞り性に優れたＡｌ−Ｍｇ系合金板とすることができる。 According to the production method of the present invention, during thin slab casting with a twin belt caster, Al—Fe, Al— (Fe · Mn) —Si, Al—Cr based compounds, etc. are crystallized uniformly and finely in the thin slab. In the final annealing, it becomes a nucleus of recrystallized grains and at the same time exhibits a pinning effect that hinders the movement of grain boundaries, so that the recrystallized grain size becomes as fine as 12 μm or less. In addition, transition metal elements such as Fe and Mn, which are supersaturated in the matrix Al, become solid solution strengthening elements together with Mg, and stop the dislocation of the rolling texture and the movement of the cell boundary during recrystallization and exist there. The rolling texture remains. As a result, the (110) orientation can be obtained, and an Al—Mg alloy plate having high r value and LDR and excellent deep drawability can be obtained.
しかもこのＡｌ−Ｍｇ系合金板は、マトリックス中におけるＦｅ、Ｍｎなどの遷移金属元素の固溶量が高く、成形後の焼付け塗装時の加熱によるによる耐力の低下が少ないため、耐焼付け軟化性にも優れている。 Moreover, this Al-Mg alloy plate has a high solid solution amount of transition metal elements such as Fe and Mn in the matrix, and there is little decrease in yield strength due to heating at the time of baking coating after molding. Is also excellent.
本発明の合金成分の意義および限定理由について説明する。本願においては、特に断りのない限り、「％」は「質量％」を意味する。 The significance and reasons for limitation of the alloy components of the present invention will be described. In the present application, “%” means “mass%” unless otherwise specified.
まず、必須要件から説明する。 First, the essential requirements will be described.
〔Ｍｇ：１〜５％〕
Ｍｇは必須成分であり、マトリックス中に固溶して固溶体強化元素として作用し、強度と成形性を付与するために添加する。Ｍｇ含有量を１〜５％と限定したのは、１％未満ではその効果が小さく、５％を越えると塑性変形による加工硬化が進み、冷間圧延時に耳割れが生じやすくいことに加え、応力腐食割れに敏感になるなどの問題が発生する可能性があるからである。Ｍｇ含有量の好ましい範囲は、１．５〜３．５％である。
[Mg: 1-5%]
Mg is an essential component, and is added to the solid solution to act as a solid solution strengthening element and impart strength and formability. The Mg content is limited to 1 to 5%. If the content is less than 1%, the effect is small. If the content exceeds 5%, work hardening by plastic deformation proceeds, and ear cracks are likely to occur during cold rolling. This is because problems such as sensitivity to stress corrosion cracking may occur. A preferable range of the Mg content is 1.5 to 3.5%.
〔Ｆｅ：０．１〜１．０％〕
Ｆｅは必須成分であり、Ｍｎ、Ｓｉと共存させることにより、薄スラブ中にＡｌ-Ｆｅ、Ａｌ-（Ｆｅ・Ｍｎ）-Ｓｉ系化合物などを均一かつ微細に晶出させる。これら微細な金属間化合物は最終焼鈍時に再結晶粒の核となり、同時に結晶粒界の移動を妨げるピン止め効果を発揮するため、再結晶粒径が１２μｍ以下と微細になり、深絞り性に優れた板となる。また、薄スラブ連続鋳造機では、溶湯の凝固冷却速度が速いため、Ｆｅが過飽和に固溶する傾向が大きくなり、均質化処理、中間焼鈍を施さない本発明においては、最終焼鈍板におけるマトリックス中のＦｅ固溶量が５０ｐｐｍ以上となる。マトリックスに固溶したＦｅは、圧延集合組織を残存させ、深絞り性に優れた板となる。しかも、成形後の焼付け塗装時の加熱による軟化の度合いが、従来法によるＤＣ材に比較して小さくなり、耐焼付け軟化性にも優れた板となる。
[Fe: 0.1 to 1.0%]
Fe is an essential component, and by coexisting with Mn and Si, Al—Fe, Al— (Fe · Mn) —Si compounds and the like are crystallized uniformly and finely in a thin slab. These fine intermetallic compounds become the core of recrystallized grains during the final annealing, and at the same time exhibit a pinning effect that hinders the movement of the crystal grain boundaries, so the recrystallized grain size becomes as fine as 12 μm or less and excellent deep drawability It becomes a plate. In the thin slab continuous casting machine, since the solidification cooling rate of the molten metal is fast, the tendency of Fe to dissolve in supersaturation increases, and in the present invention in which homogenization treatment and intermediate annealing are not performed, The Fe solid solution amount becomes 50 ppm or more. Fe dissolved in the matrix leaves a rolling texture and becomes a plate excellent in deep drawability. In addition, the degree of softening due to heating during baking after molding is smaller than that of a DC material obtained by the conventional method, and the plate is excellent in baking softening resistance.
Ｆｅ含有量を０．１〜１．０％と限定したのは、０．１％未満ではその効果が小さく、１．０％を越えると鋳造時に粗大な金属間化合物を生じやすく、深絞り成形性を劣化させる可能性があるからである。Ｆｅ含有量のさらに好ましい範囲は、０．１５〜０．５％である。 The reason for limiting the Fe content to 0.1 to 1.0% is that the effect is small if it is less than 0.1%, and if it exceeds 1.0%, a coarse intermetallic compound is likely to be produced at the time of casting. This is because there is a possibility of deteriorating the performance. A more preferable range of the Fe content is 0.15 to 0.5%.
〔Ｔｉ：０．００５〜０．１％〕
Ｔｉは必須成分であり、薄スラブの結晶粒微細化剤として作用し、スラブ割れ等の鋳造欠陥を確実に防止することができる。Ｔｉ含有量が０．００５％未満では、その効果が十分でなく、Ｔｉ含有量が０．１０％を超える場合には、鋳造時にＴｉＡｌ3等の粗大な金属間化合物が生成するため、曲げ性が著しく低下する。したがって、Ｔｉ含有量は０．００５〜０．１０％とする。Ｔｉ含有量の好ましい範囲は、０．００５〜０．０５％である。
[Ti: 0.005 to 0.1%]
Ti is an essential component and acts as a grain refiner for thin slabs, and can reliably prevent casting defects such as slab cracking. When the Ti content is less than 0.005%, the effect is not sufficient, and when the Ti content exceeds 0.10%, a coarse intermetallic compound such as TiAl 3 is generated during casting, so that the bendability is increased. Is significantly reduced. Therefore, the Ti content is 0.005 to 0.10%. A preferred range for the Ti content is 0.005 to 0.05%.
〔Ｂ：０．０００５〜０．０１％〕
Ｂは必須成分であり、鋳塊の結晶粒微細化剤としてのロッドハードナー（例えば、Ａｌ-５％Ｔｉ-１％Ｂ）を添加することで、必然的に混入する。Ｂは、溶湯中で必須元素であるＴｉと混在することで、鋳塊の結晶粒微細化効果が飛躍的に向上する。Ｂ含有量が０．０００５％未満の場合には、結晶粒微細化効果が十分でなく、スラブ割れ等の鋳造欠陥を確実に防止することが困難である。Ｂ含有量が０．０１％を超える場合には、鋳塊の結晶粒微細化効果が飽和するだけではなく、最終焼鈍板において、余剰のＴｉＢ2の凝集体が介在物として作用する場合があり、深絞り加工時に板表面キズを発生させるなど成形性を低下させる虞がある。
[B: 0.0005 to 0.01%]
B is an essential component and is inevitably mixed by adding a rod hardener (for example, Al-5% Ti-1% B) as a crystal grain refining agent for the ingot. When B is mixed with Ti which is an essential element in the molten metal, the crystal grain refining effect of the ingot is dramatically improved. When the B content is less than 0.0005%, the crystal grain refining effect is not sufficient, and it is difficult to reliably prevent casting defects such as slab cracks. When the B content exceeds 0.01%, not only the crystal grain refining effect of the ingot is saturated, but excessive TiB 2 aggregates may act as inclusions in the final annealed plate. Further, there is a possibility that the formability may be deteriorated by causing scratches on the plate surface during deep drawing.
〔不可避的不純物〕
不可避的不純物は、アルミニウム地金、返り材、フラックスなどに含まれる不純物元素、或いは溶湯中のＭｇによる炉材シリカの還元溶出、溶製治具と溶湯との反応などが原因で混入する。Ｓｉ、Ｃｕ、Ｎｉ、Ｚｎ、Ｇａ、Ｖ、Ｃａ、Ｎａなどが代表的な元素である。
[Inevitable impurities]
Inevitable impurities are mixed due to the impurity element contained in the aluminum ingot, the return material, the flux, or the like, or the reduction elution of the furnace material silica by Mg in the molten metal, the reaction between the melting jig and the molten metal, or the like. Si, Cu, Ni, Zn, Ga, V, Ca, Na, etc. are typical elements.
特にＳｉは返り材から多く混入するので配合には注意を要する。 過剰に含有すると、Ｍｇ2ＳｉやＡｌ-（Ｆｅ・Ｍｎ）-Ｓｉなどの晶出物が増加して、深絞り成形性を劣化させる。したがって、Ｓｉ含有量は０．２％未満に制限すべきである。Ｓｉ含有量の更に好ましい範囲は０．１５％未満である。 In particular, since Si is mixed in a large amount from the return material, it is necessary to pay attention to the formulation. If excessively contained, increasing the crystallized substances, such as Mg 2 Si and Al- (Fe · Mn) -Si, deteriorating the deep drawability. Therefore, the Si content should be limited to less than 0.2%. A more preferable range of the Si content is less than 0.15%.
〔マトリクス中のＦｅ固溶量：５０ｐｐｍ以上〕
マトリクス中のＦｅの固溶量を５０ｐｐｍ以上に限定したのは以下の理由による。
[Fe solid solution in the matrix: 50 ppm or more]
The reason why the solid solution amount of Fe in the matrix is limited to 50 ppm or more is as follows.
すなわち、マトリクス中に固溶したＦｅは、再結晶の際に圧延集合組織を残存させ、深絞り成形性を高める効果がある。同時に、板成形後、焼付け塗装の加熱時に転位の回復を妨げて強度低下を抑制する効果もある。Ｆｅ固溶量が５０ｐｐｍ未満であると、これらの効果が十分に得られない。 That is, Fe dissolved in the matrix has the effect of increasing the deep drawability by leaving the rolling texture during recrystallization. At the same time, after plate forming, there is also an effect of inhibiting the recovery of dislocation during heating of the baking coating and suppressing the strength reduction. If the Fe solid solution amount is less than 50 ppm, these effects cannot be obtained sufficiently.
次に、任意要件を説明する。 Next, optional requirements will be described.
〔Ｃｒ：０．０５〜０．４％〕
Ｃｒは任意成分であり、鋳造時に５μｍ以下のサイズのＡｌ-Ｃｒ系金属間化合物を均一かつ微細に晶出させる。これら微細な金属間化合物は最終焼鈍時に再結晶粒の核となり、同時に結晶粒界の移動を妨げるピン止め効果を発揮するため、製造条件（特に最終焼鈍温度など）を厳しく制限しなくとも再結晶粒径が容易に１２μｍ以下に微細化する。
[Cr: 0.05-0.4%]
Cr is an optional component, and Al—Cr intermetallic compounds having a size of 5 μm or less are crystallized uniformly and finely during casting. These fine intermetallic compounds become the cores of recrystallized grains during final annealing, and at the same time exert a pinning effect that hinders the movement of grain boundaries, so recrystallization is possible without severely limiting production conditions (especially final annealing temperature). The particle size is easily reduced to 12 μm or less.
したがって、本発明の合金は０．０５〜０．４０％のＣｒを含有することが好ましい。Ｃｒ含有量が０．０５％未満ではその効果が十分でなく、再結晶粒の粒径を１２μｍ以下に微細化するには上記したような製造条件を厳しく制限しなくてはならない。再結晶粒径が１２μｍを超えると肌荒れ性が低下する。一方、Ｃｒ含有量が０．４０％を超えると鋳造時に粗大な金属間化合物を生じやすく、深絞り性を劣化させる。 Therefore, the alloy of the present invention preferably contains 0.05 to 0.40% Cr. If the Cr content is less than 0.05%, the effect is not sufficient, and the production conditions as described above must be severely limited in order to reduce the grain size of the recrystallized grains to 12 μm or less. When the recrystallized grain size exceeds 12 μm, the rough skin property decreases. On the other hand, if the Cr content exceeds 0.40%, a coarse intermetallic compound is likely to be produced during casting, and the deep drawability is deteriorated.
〔Ｍｎ：０．０５〜０．５％〕
Ｍｎは任意成分であり、Ｆｅ、Ｓｉとともに鋳造時に５μｍ以下のサイズのＡｌ-（Ｆｅ・Ｍｎ）-Ｓｉ系金属間化合物を均一かつ微細に晶出させる。これら微細な金属間化合物は最終焼鈍時に再結晶粒の核となり、同時に結晶粒界の移動を妨げるピン止め効果を発揮するため、前記のような製造条件を厳しく制限しなくとも、再結晶粒径が容易に１２μｍ以下に微細化する。また、薄スラブ連続鋳造機では、溶湯の凝固冷却速度が速いため、Ｍｎが過飽和に固溶する傾向が大きくなり、均質化処理、中間焼鈍を施さない本発明においては、最終焼鈍板におけるマトリックス中のＭｎ固溶量が５０ｐｐｍ以上となる。マトリックスに固溶されたＭｎは圧延集合組織を残存させ、深絞り性に優れた板となる。しかも、成形後の焼付け塗装時の加熱による軟化の度合いが、従来法によるＤＣ材に比較して小さくなり、耐焼付け軟化性にも優れた板となる。
[Mn: 0.05 to 0.5%]
Mn is an optional component, and together with Fe and Si, Al— (Fe · Mn) —Si intermetallic compounds having a size of 5 μm or less are crystallized uniformly and finely during casting. These fine intermetallic compounds become the core of recrystallized grains during the final annealing, and at the same time exert a pinning effect that hinders the movement of grain boundaries. However, it is easily refined to 12 μm or less. Also, in the thin slab continuous casting machine, the solidification cooling rate of the molten metal is fast, so the tendency of Mn to dissolve in supersaturation increases, and in the present invention in which homogenization treatment and intermediate annealing are not performed, The Mn solid solution amount is 50 ppm or more. Mn dissolved in the matrix leaves a rolling texture and becomes a plate excellent in deep drawability. In addition, the degree of softening due to heating during baking after molding is smaller than that of a DC material obtained by the conventional method, and the plate is excellent in baking softening resistance.
したがって、本発明の合金は０．０５〜０．５０％のＭｎを含有することが好ましい。Ｍｎ含有量が０．０５％未満ではその効果が十分でなく、再結晶粒の粒径を１２μｍ以下に微細化するには上記したような製造条件を厳しく制限しなくてはならない。再結晶粒の粒径が１２μｍを超えると肌荒れ性が低下する。０．５０％を超えると鋳造時に粗大な金属間化合物を生じやすく、深絞り性を劣化させる。 Therefore, the alloy of the present invention preferably contains 0.05 to 0.50% Mn. If the Mn content is less than 0.05%, the effect is not sufficient, and the production conditions as described above must be severely restricted in order to reduce the grain size of the recrystallized grains to 12 μm or less. When the grain size of the recrystallized grains exceeds 12 μm, the rough skin property decreases. If it exceeds 0.50%, a coarse intermetallic compound is likely to be produced during casting, and the deep drawability is deteriorated.
本発明の製造方法の諸条件を限定した理由を説明する。 The reason why the conditions of the production method of the present invention are limited will be described.
以下の説明においては、製造工程順に記載し、必須要件と任意要件と明記した。 In the following explanation, it describes in order of a manufacturing process, and specified it as an essential requirement and an arbitrary requirement.
〔双ベルト鋳造機により連続鋳造して薄スラブとし＜必須要件＞〕
本発明の高温高速成形性に優れたＡｌ−Ｍｇ系合金板の製造に用いる薄スラブは双ベルト式鋳造機により鋳造する。
[Continuous casting by twin belt casting machine to make a thin slab <required requirement>]
The thin slab used for the production of the Al—Mg alloy plate excellent in high-temperature high-speed formability of the present invention is cast by a twin-belt casting machine.
双ベルト式鋳造機とは、上下に対面し水冷されている一対の回転ベルト間に溶湯を注湯してベルト面からの冷却で溶湯を凝固させてスラブとし、ベルトの反注湯側より該スラブを連続して引き出してコイル状に巻き取る方式の鋳造機である。 The twin-belt casting machine is a method in which molten metal is poured between a pair of rotating belts facing up and down and cooled by water, and the molten metal is solidified by cooling from the belt surface to form a slab. This is a casting machine that draws out a slab continuously and winds it up in a coil.
〔双ベルト式鋳造機により鋳造した厚さ３〜１５ｍｍのスラブを巻き取り（任意要件）〕
〔スラブ厚み１／４における凝固冷却速度が２０〜１５０℃／sec（任意要件）〕
本発明においては、鋳造する薄スラブの厚さは３〜１５ｍｍとすることが好ましい。この範囲の厚さであれば、スラブ厚み１／４において２０〜１５０℃/sec程度の凝固冷却速度を容易に確保できるので、均一な鋳造組織を形成し易く、マトリックス中へのＦｅ、Ｍｎなどの遷移金属元素の固溶量を確保することが容易にできる。また、鋳造凝固時に生成される金属間化合物のサイズを５μｍ以下に抑え易くなり、結果的に最終焼鈍後の再結晶粒の平均粒径を１２μｍ以下に制御することが容易になる。
[Take up 3-15mm thick slab cast by twin belt casting machine (optional requirement)]
[Solidification cooling rate at slab thickness 1/4 is 20 to 150 ° C./sec (optional requirement)]
In the present invention, the thickness of the cast thin slab is preferably 3 to 15 mm. If the thickness is within this range, a solidification cooling rate of about 20 to 150 ° C./sec can be easily secured at a slab thickness of 1/4, so that a uniform cast structure can be easily formed, such as Fe and Mn in the matrix. It is easy to secure a solid solution amount of the transition metal element. Moreover, it becomes easy to suppress the size of the intermetallic compound produced | generated at the time of casting solidification to 5 micrometers or less, and it becomes easy to control the average particle diameter of the recrystallized grain after final annealing to 12 micrometers or less as a result.
上記のスラブ厚さ範囲は、ベルト式鋳造機の実行面からも最適である。すなわち、スラブ厚さが３ｍｍ未満であると、単位時間当りに鋳造機を通過するアルミニウム合金量が少ないため、鋳造が困難になる。スラブ厚さが１５ｍｍを超えると、コイルとして巻き取ることが困難になる。 The above slab thickness range is also optimal from the practical aspect of the belt type casting machine. That is, when the slab thickness is less than 3 mm, casting becomes difficult because the amount of aluminum alloy passing through the casting machine per unit time is small. When the slab thickness exceeds 15 mm, it becomes difficult to wind it as a coil.
〔薄スラブに均質化処理および中間焼鈍を施すことなく＜必須要件＞〕
本発明においては、コイルに巻き取った薄スラブに均質化処理および中間焼鈍のいずれも施すことなく最終板厚まで冷間圧延する。均質化処理、中間焼鈍を施さないため、マトリックス中に過飽和に固溶されたＦｅ、Ｍｎは、そのまま維持され、耐焼付け軟化性に優れた板を製造できる。
[Necessary homogenization and intermediate annealing of thin slabs <required requirement>]
In the present invention, the thin slab wound around the coil is cold-rolled to the final plate thickness without any homogenization treatment or intermediate annealing. Since the homogenization and intermediate annealing are not performed, Fe and Mn dissolved in supersaturation in the matrix are maintained as they are, and a plate excellent in bake resistance and softening can be manufactured.
また、この製造方法では、従来法による複雑な工程のうち、両面面削、均質化処理、熱間圧延、中間焼鈍などの工程が省略されるため、製造コストを低く抑えることが可能である。 Moreover, in this manufacturing method, steps such as double-sided chamfering, homogenization treatment, hot rolling, and intermediate annealing among the complicated steps according to the conventional method are omitted, so that the manufacturing cost can be kept low.
〔連続焼鈍炉により保持温度４００〜５２０℃で行う（任意要件）〕
本願発明においては、冷間圧延後に最終焼鈍を行う。この最終焼鈍は、バッチ焼鈍炉で実施してもよいが、連続焼鈍炉（ＣＡＬ）で実施する方が好ましい。連続焼鈍炉（ＣＡＬ）とは、コイルを連続的に溶体化処理等するための設備であり、熱処理を施すための誘導加熱装置や水冷するための水槽および空冷するためのエアノズル等を備えたことを特徴としている。最終焼鈍温度は４００〜５２０℃の範囲が好ましい。４００℃未満であると、再結晶に必要なエネルギー供給が少ないため、再結晶が十分に起きることが困難になり、微細な再結晶組織を得ることが困難になる。しかし、最終焼鈍温度が５２０℃を超えると、再結晶粒径が１２μｍを超えて粗大化し易くなり、微細な再結晶組織を得ることが困難になる。
[Performed at a holding temperature of 400 to 520 ° C. in a continuous annealing furnace (optional requirement)]
In the present invention, final annealing is performed after cold rolling. This final annealing may be performed in a batch annealing furnace, but is preferably performed in a continuous annealing furnace (CAL). Continuous annealing furnace (CAL) is equipment for continuously solution treatment of coils, etc., equipped with induction heating device for heat treatment, water tank for water cooling, air nozzle for air cooling, etc. It is characterized by. The final annealing temperature is preferably in the range of 400 to 520 ° C. If it is less than 400 ° C., the energy supply required for recrystallization is small, so that it is difficult for recrystallization to occur sufficiently, and it becomes difficult to obtain a fine recrystallized structure. However, when the final annealing temperature exceeds 520 ° C., the recrystallized grain size exceeds 12 μm, and it becomes easy to coarsen, and it becomes difficult to obtain a fine recrystallized structure.
連続焼鈍炉における焼鈍温度での保持時間は４０秒以内とすることが好ましい。４０秒以上の保持時間の場合、再結晶粒が粗大化し易くなり、微細な再結晶組織を得ることが困難になる。 The holding time at the annealing temperature in the continuous annealing furnace is preferably within 40 seconds. When the holding time is 40 seconds or longer, the recrystallized grains are likely to be coarsened, and it becomes difficult to obtain a fine recrystallized structure.
〔バッチ焼鈍炉により保持温度３００〜４００℃で行う（任意要件）〕
この最終焼鈍をバッチ焼鈍炉で実施する場合、最終焼鈍温度は３００〜４００℃の範囲とすることが好ましい。３００℃未満であると、再結晶に必要なエネルギー供給が少ないため、再結晶が不十分に起きることが困難になり、微細な再結晶組織を得ることが困難になる。しかし、最終焼鈍温度が４００℃を超えると、再結晶粒径が１２μｍを超えて粗大化し易くなり、微細な再結晶組織を得ることが困難になる。
[Performed at a holding temperature of 300 to 400 ° C. with a batch annealing furnace (optional requirement)]
When this final annealing is performed in a batch annealing furnace, the final annealing temperature is preferably in the range of 300 to 400 ° C. When the temperature is lower than 300 ° C., the energy supply necessary for recrystallization is small, so that it becomes difficult for recrystallization to occur insufficiently, and it becomes difficult to obtain a fine recrystallized structure. However, when the final annealing temperature exceeds 400 ° C., the recrystallized grain size easily exceeds 12 μm and becomes coarse, and it becomes difficult to obtain a fine recrystallized structure.
バッチ焼鈍炉における焼鈍温度での保持時間は０．５〜１２時間とすることが好ましい。保持時間が０．５時間未満の場合、コイルの実体温度が炉内雰囲気温度まで到達しない虞れがある。保持時間が１２時間を超えても、微細な再結晶組織を発現させる作用が更に増加することはなく、単に生産性の低下を招くだけである。 The holding time at the annealing temperature in the batch annealing furnace is preferably 0.5 to 12 hours. If the holding time is less than 0.5 hour, the actual temperature of the coil may not reach the furnace atmosphere temperature. Even if the holding time exceeds 12 hours, the effect of developing a fine recrystallized structure is not further increased, and the productivity is simply lowered.
本発明例として、表１に「ＣＣ材」と示す合金組成のアルミニウム合金溶湯を双ベルト式連続鋳造機で１０ｍｍの厚みの薄スラブを鋳造してコイルに巻き取った。鋳造した薄スラブはその後、均質化処理、中間焼鈍を行わず、最終板厚１ｍｍまで冷間圧延した。 As an example of the present invention, a molten aluminum alloy having an alloy composition shown as “CC material” in Table 1 was cast into a thin slab having a thickness of 10 mm with a twin belt type continuous casting machine and wound around a coil. Thereafter, the cast thin slab was cold-rolled to a final thickness of 1 mm without performing homogenization and intermediate annealing.
比較例として、表１に「ＤＣ材」と示す合金組成のアルミニウム合金溶湯をＤＣ鋳造機にて１０００ｍｍ×５００ｍｍ×４０００ｍｍのスラブに鋳造し、両面面削した後、熱処理炉にて４５０℃×１２ｈｒｓの均質化処理を行い、引き続き熱間圧延機にて、熱延を行って、６ｍｍ厚さの熱間圧延板をコイルに巻き取った。その後、中間焼鈍することなく、最終板厚１ｍｍまで冷間圧延した。 As a comparative example, a molten aluminum alloy having an alloy composition shown in Table 1 as “DC material” was cast into a 1000 mm × 500 mm × 4000 mm slab with a DC casting machine, both sides were cut, and then 450 ° C. × 12 hrs in a heat treatment furnace. Next, hot rolling was performed with a hot rolling mill, and a 6 mm thick hot rolled plate was wound around the coil. Then, it cold-rolled to the final board thickness of 1 mm, without carrying out intermediate annealing.
本発明例のＣＣ材冷延板および比較例のＤＣ材冷延板を、いずれも連続焼鈍炉（ＣＡＬ：continuous annealing line）にて、保持温度４２５℃で焼鈍を行った。 The CC cold-rolled sheet of the inventive example and the DC cold-rolled sheet of the comparative example were both annealed at a holding temperature of 425 ° C. in a continuous annealing furnace (CAL).
上記焼鈍後の各板材からミクロ組織観察用試料を採取して断面を研磨し、クロスカット法で再結晶粒径の測定を行った。さらにマトリックス中のＦｅ固溶量、Ｍｎ固溶量を熱フェノール法にて測定した。結果を表２に示す。ＣＣ材の再結晶粒径は１２μｍ以下であり、Ｆｅ、Ｍｎの固溶量は各々５０ｐｐｍ以上である。 A sample for microstructural observation was collected from each plate after the annealing, the cross section was polished, and the recrystallized grain size was measured by a cross-cut method. Further, the Fe solid solution amount and the Mn solid solution amount in the matrix were measured by a hot phenol method. The results are shown in Table 2. The recrystallized grain size of the CC material is 12 μm or less, and the solid solution amounts of Fe and Mn are each 50 ppm or more.
同じく上記焼鈍後の各板材から、Ｌ方向、ＬＴ方向、圧延４５°方向の引張試験片を切り出し加工して、引張試験を行い、引張強さ、耐力、伸びを測定し、平均値を算出した。結果を表３に示す。 Similarly, from each of the plate materials after the annealing, a tensile test piece in the L direction, the LT direction, and the rolling 45 ° direction was cut out and subjected to a tensile test, and the average value was calculated by measuring the tensile strength, the yield strength, and the elongation. . The results are shown in Table 3.
またｒ値（ランクフォード値）については、前記３方向の平均値(mean value)であるｒm値により、ｎ値（加工硬化指数）についても前記３方向の平均値であるｎm値により評価した。結果を表３に示す。 For also r value (Lankford value) evaluation, the r m values wherein a three-way average (mean value), the n m value is an average value of the three-way also n value (work hardening exponent) did. The results are shown in Table 3.
表３に示す各結果から、ＣＣ材はＤＣ材に比べ、引張強さ、耐力、ｒm値ともに高いが、伸び、ｎm値についてはＣＣ材もＤＣ材と同等であることが判った。 From each result shown in Table 3, CC material compared to DC material, tensile strength, yield strength, but high r m values for both, elongation, for n m value was found that CC material also is equivalent to DC material.
さらに上記焼鈍後の各板材から、φ６８．０〜７４．６ｍｍの範囲で９種類のサイズの円盤を打ち抜き、深絞り性評価試験を行って限界絞り比（ＬＤＲ）の測定を行った。なお、シワ押さえ力は５００ｋｇとし、ポンチ径はφ３３ｍｍであった。結果を表３に示す。 Furthermore, nine types of discs were punched from each plate after the annealing in the range of φ68.0 to 74.6 mm, and a deep drawability evaluation test was performed to measure a limit drawing ratio (LDR). The wrinkle pressing force was 500 kg, and the punch diameter was 33 mm. The results are shown in Table 3.
ＤＣ材の限界絞り比（ＬＤＲ）が２．１１であるのに対し、ＣＣ材の限界絞り比（ＬＤＲ）は２．１７であり、ＣＣ材はＤＣ材に比べ、深絞り性に優れていることが判った。 The limit drawing ratio (LDR) of the DC material is 2.11, whereas the limit drawing ratio (LDR) of the CC material is 2.17, and the CC material is superior in the deep drawing property compared to the DC material. I found out.
さらに上記焼鈍後の各板材引張試験片について、成形後の耐焼付軟化性をシミュレートするため、５％、１０％の予歪を加えて予歪材とし、更にこれら予歪材の一部について１８０℃×３０ｍｉｎの熱処理（加熱）を行った。熱処理前、熱処理後の予歪材について引張り試験を行った。結果を表４に示す。 Furthermore, in order to simulate the seizure softening resistance after forming the above-mentioned annealed sheet material tensile test pieces, 5% and 10% pre-strains are added to form pre-strained materials, and a part of these pre-strained materials. Heat treatment (heating) was performed at 180 ° C. for 30 minutes. A tensile test was performed on the pre-strained material before and after heat treatment. The results are shown in Table 4.
ＣＣ材はＤＣ材に比べ、引張強度・耐力について軟化率が低く、耐焼付け軟化性に優れていることが判った。 It was found that the CC material had a lower softening rate in terms of tensile strength and proof stress than the DC material, and was excellent in anti-seizure softening property.
以上説明したように、本発明によれば、複雑な製造工程を必要とせずに、深絞り性と耐焼付け軟化性とを同時に高めた成形加工用アルミニウム合金板およびその製造方法が提供される。 As described above, according to the present invention, there is provided an aluminum alloy plate for forming and a method for producing the same that have improved deep drawability and anti-seizure softening properties without requiring a complicated production process.
Claims (5)
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| JP4534573B2 (en) * | 2004-04-23 | 2010-09-01 | 日本軽金属株式会社 | Al-Mg alloy plate excellent in high-temperature high-speed formability and manufacturing method thereof |
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