JP3857418B2 - Method for producing aluminum alloy semi-hard material with excellent formability - Google Patents
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Description
【０００１】
【発明の属する技術分野】
本発明は、成形性に優れるアルミニウム合金半硬質材を高歩留まりで製造する方法に関する。
【０００２】
【従来の技術】
一般に、アルミニウム合金半硬質材には、加工硬化材を焼鈍軟化させた焼鈍調質材と完全焼鈍材を加工硬化させた加工調質材の２種がある。前者はＨ２Ｘ、後者はＨ１ＸとＪＩＳ表記される。
前記焼鈍調質材は加工調質材より伸びが大きく成形性に優れるので、プレス成形用には、通常、焼鈍調質材が使用され、特に、比較的強度の高いＨ２４は代表的半硬質材として多用されている。
前記焼鈍調質材は、所定組成の合金鋳塊に均質化処理、熱間圧延、冷間圧延を順に施し、前記冷間圧延後、半軟化温度で焼鈍（調質焼鈍）して製造される。
【０００３】
【発明が解決しようとする課題】
最近、成形加工の自動化および高速化が進み、半硬質材には品質および特性に関して変動の極小化が求められ、従来の半硬質材では対応できず、より成形性に優れる材料の開発、さらに材料の成形可能限界の向上が必須になってきている。
【０００４】
ところで、成形加工材として汎用性の高い、厚さが０．５〜２ｍｍのＪＩＳ−１１００、１２００など（いずれも低強度材）の半硬質材は、中間焼鈍を入れずに冷間圧延した材料を調質焼鈍して製造されている。
しかし、前記冷間圧延材は、冷間加工度が過大なため調質焼鈍で軟化が急激に起き、所要強度が得られる焼鈍温度範囲が極めて狭く、また前記温度範囲は熱間圧延状況によっても変化する。このため、焼鈍不足や過焼鈍などの焼鈍不良が多く、製造歩留まりが低下するという問題がある。
【０００５】
一方、中間焼鈍を入れた冷間圧延材は、調質焼鈍での軟化が緩やかで、所要強度が得られる調質焼鈍温度範囲が広くとれ、しかも熱間圧延状況による影響も小さく、従って焼鈍不良も少ない。しかしこの焼鈍調質材は伸びが低く成形性に劣るという問題がある。
このようなことから、本発明者等は、鋳塊の均質化処理、中間焼鈍、最終冷間圧延率、調質焼鈍などの条件について詳細に検討し、成形性に優れるアルミニウム合金半硬質材を高歩留まりで製造する方法を見い出すことに成功した。
本発明は、成形性に優れるアルミニウム合金半硬質材（調質焼鈍材）を高歩留まりで製造することを目的とする。
【０００６】
【課題を解決するための手段】
本発明は、Ｆｅ０．２〜０．９wt％、Ｓｉ０．１〜０．３wt％を含有し、前記ＦｅとＳｉの含有量の比（Ｆｅ／Ｓｉ）が２．０以上、前記ＦｅとＳｉの含有量の合計が１．０wt％以下であり、必要に応じてＣｕ０．０５〜０．２wt％を含有し、さらに必要に応じてＴｉ０．００５〜０．０５wt％、Ｂ０．００１〜０．０１wt％のうちの１種または２種を含有し、残部がＡｌおよび不可避不純物からなるアルミニウム合金鋳塊に均質化処理を施し、その後熱間圧延、中間焼鈍を入れる冷間圧延、調質焼鈍を順に施すアルミニウム合金半硬質材の製造方法であって、前記均質化処理を５４０〜６１０℃の温度で１〜１５時間施し、少なくとも最終中間焼鈍を軟化率が２０〜７０％になるように施し、最終中間焼鈍後の冷間圧延を圧延率５０％以下で施し、調質焼鈍を２００〜２６０℃の温度で施すことを特徴とする成形性に優れるアルミニウム合金半硬質材の製造方法である。
【０００７】
【発明の実施の形態】
本発明で用いるＡｌ−Ｆｅ−Ｓｉ合金について説明する。
Ｆｅは強度向上に寄与して成形性を高め、また熱間圧延や中間焼鈍などで再結晶粒を微細化して成形性を向上させる。さらに肌荒れを防止して成形品の表面品質を高める。
Ｆｅの添加量を０．２〜０．９wt％に規定する理由は、０．２wt％未満ではその効果が十分に得られず、０．９wt％を超えるとその効果が飽和し、また他の添加元素或いは不純物との間で粗大な金属間化合物を生成して表面欠陥の原因になり、また成形性を害する。
【０００８】
ＳｉはＡｌマトリックス中に固溶して強度向上に寄与する。
Ｓｉの含有量を０．１〜０．３wt％に規定する理由は、０．１wt％未満ではその効果が十分に得られず、０．３wt％を超えるとＦｅとの間で粗大金属間化合物を生成して成形性を害するためである。
【０００９】
適量のＦｅとＳｉはＡｌとともに金属間化合物を形成して熱間圧延や中間焼鈍などで形成される再結晶粒を微細化して成形性を向上させる。しかし、その量があまり多くなると、金属間化合物が粗大化して延性が低下し成形性が低下する。そのためＦｅとＳｉの含有量の合計は１．０wt％以下にする。
前記金属間化合物量はＦｅとＳｉの比によっても影響される。すなわち、過剰Ｓｉは前記金属間化合物の生成を妨げ、ひいては再結晶核の形成を妨げて、再結晶粒を粗大化させる。このためＦｅとＳｉの含有量の比（Ｆｅ／Ｓｉ）は２．０以上とＦｅの含有比率を高くする。
【００１０】
本発明では前記Ａｌ−Ｆｅ−Ｓｉ合金に、必要に応じてＣｕを含有させる。
Ｃｕは強度を向上させて成形性を高める。またアルマイト処理する場合は、その色調を均質にする。
Ｃｕの含有量を０．０５〜０．２wt％に規定する理由は、０．０５wt％未満ではその効果が十分に得られず、０．２wt％を超えると耐食性が低下するためである。
【００１１】
本発明では、前記Ａｌ−Ｆｅ−Ｓｉ合金に、必要に応じてＴｉ、Ｂのうちの１種または２種を含有させる。
Ｔｉは鋳塊組織を微細化して、圧延材表面の肌荒れや外観の不均一性を改善する。その含有量を０．００５〜０．０５wt％に規定する理由は、０．００５wt％未満ではその効果が十分に得られず、０．０５wt％を超えると溶解鋳造時に巨大なＡｌ−Ｔｉ系金属間化合物が生成し、これが圧延後も残存して成形品の表面傷の原因になり、また成形性を害する。
ＢはＴｉの微細化効果を助長する。Ｂが０．００１wt％未満ではその助長効果が十分に得られず、０．０１wt％を超えると溶解鋳造時に巨大なＴｉ−Ｂ系金属間化合物が生成し、これが圧延後も残存して成形品の表面傷の原因になる。
本発明では、前記Ｃｕと、ＴｉまたはＢの１種以上とを共存させても、それぞれが前述と同じ効果を発現する。
【００１２】
本発明の半硬質材は、前述のＡｌ−Ｆｅ−Ｓｉ−（Ｃｕ）−（Ｔｉ）−（Ｂ）合金を鋳造し、得られる鋳塊に均質化処理、熱間圧延、中間焼鈍を入れる冷間圧延を順に施し、最後に調質焼鈍を施して製造される。
前記均質化処理により、鋳塊組織中の溶質元素の偏析が均質化し、またＦｅ、Ｓｉなどの金属間化合物の分布が適正化される。また均質化処理により金属間化合物が適度に粗大化し、この適度に粗大化した金属間化合物は、熱間圧延や中間焼鈍で再結晶核として有効に機能して、微細な再結晶組織を形成する。
【００１３】
前記均質化処理を５４０〜６１０℃の温度で１〜１５時間施す理由は、５４０℃未満では金属間化合物が適度に粗大化せず、このため再結晶核となる金属間化合物が減少して再結晶粒が粗大化し、成形性や外観が損なわれ、６１０℃を超えると鋳塊に変形や膨れなどが生じ、のちに材料欠陥の原因になる。均質化処理時間が１時間未満では均質化処理効果が十分に得られず、１５時間を超えるとその効果が飽和してコスト的に不利になるためである。特に望ましい均質化処理時間は２〜６時間である。
【００１４】
均質化処理後の熱間圧延は常法に準じて行う。また熱間圧延後の冷間圧延では中間焼鈍を施す。中間焼鈍を入れた冷間圧延材は、前述のように、所要強度を得るための調質焼鈍温度範囲を広くとれる。
従来、この中間焼鈍は完全焼鈍（完全再結晶）させて行っていたが、完全焼鈍を行う場合は、中間焼鈍前の冷間圧延率を十分に大きくしておかないと、中間焼鈍後の再結晶粒が大きくなり肌荒れが生じ易くなる。
このため、本発明では、少なくとも最終中間焼鈍は完全再結晶させずに、部分再結晶する条件、つまり軟化率が２０〜７０％になる条件で施す。
【００１５】
本発明において、少なくとも最終中間焼鈍を軟化率が２０〜７０％になるように施す理由は、前記軟化率が２０％未満では、調質焼鈍後に、成形性を良好にする大きい伸びが得られず、７０％を超えると調質焼鈍において軟化が急激に起きて焼鈍不良が生じ易くなるためで、特に望ましい軟化率は３０〜６０％である。ここで、軟化率は〔（Ａ−Ｂ）／Ａ〕の式で表される。但し、Ａは中間焼鈍前の材料の硬さ、Ｂは中間焼鈍後の材料の硬さである。
【００１６】
軟化率が２０〜７０％の結晶組織は、微細な再結晶粒と亜結晶粒界が発達した未再結晶粒とが混在したものである。
前記２０〜７０％の軟化率は、２２０〜２８０℃の温度で中間焼鈍することにより得られる。すなわち、中間焼鈍温度が２２０℃未満では未再結晶粒の亜結晶粒界が十分に発達せず、２８０℃を超えると急激に再結晶して軟化率を２０〜７０％に制御するのが困難になる。
【００１７】
本発明で、最終中間焼鈍後の冷間圧延を圧延率５０％以下で施す理由は、圧延率が５０％を超えると調質焼鈍後に伸びが十分回復せず、必要とする成形性が得られないためである。
【００１８】
本発明で、調質焼鈍を２００〜２６０℃の温度で施す理由は、２００℃未満では成形性を良好にする大きい伸びが得られず、２６０℃を超えると材料が過度に軟化して成形性が悪化するためである。
【００１９】
【実施例】
以下に本発明を実施例により詳細に説明する。
（実施例１）
表１に示す本発明規定内組成のアルミニウム合金鋳塊（厚さ５００ｍｍ、幅１２００ｍｍ、長さ４０００ｍｍ）に、表２に示すＡの条件で、均質化処理、熱間圧延、中間焼鈍、最終冷間圧延、調質焼鈍を順に施して、厚さ１．０ｍｍの半硬質板を製造した。均質化処理時間は、いずれも４時間とした。
【００２０】
（比較例１）
表１に示す本発明規定外組成のアルミニウム合金鋳塊を用いた他は、実施例１と同じ方法により厚さ１．０ｍｍの半硬質板を製造した。
【００２１】
実施例１と比較例１で製造した各々の半硬質板について、引張強さ、伸び、成形性を調べた。
成形性はエリクセン試験により調べ、圧延板に割れが入るまでのポンチの移動距離（エリクセン値）が１５ｍｍ未満のものは不良（×）、１５ｍｍ以上のものは良好（○）と評価した。
結果を表３に示す。表３には中間焼鈍後の軟化率を併記した。
【００２２】
【表１】
【表２】
【表３】
表３より明らかなように、本発明例のNo.1〜3 は、いずれも引張強さおよび伸びが高く、従って成形性に優れた。冷間圧延中に中間焼鈍を入れたので調質焼鈍温度範囲が広くなり焼鈍不良は生じなかった。
これに対し、比較例のNo.4〜8 は、合金組成が本発明組成外のため、いずれも引張強さおよび伸びが低く、従って成形性が劣った。
【００２６】
（実施例２）
表１に示したNo.1の組成のアルミニウム合金鋳塊を用い、表２に示したＢ〜Ｅの製造条件により厚さ１．０ｍｍの半硬質板を製造した。
【００２７】
（比較例２）
表１に示したNo.1の組成のアルミニウム合金鋳塊を用い、表２に示したＦ〜Ｌの製造条件により厚さ１．０ｍｍの半硬質板を製造した。
【００２８】
実施例２または比較例２で製造した各々の半硬質板について、引張強さ、伸び、および成形性を実施例１と同じ方法により調査した。
結果を表４に示す。表４には中間焼鈍後の軟化率を併記した。
【００２９】
【表４】
表４より明らかなように、本発明例のNo.9〜13は、いずれも引張強さおよび伸びが高く、従って成形性に優れた。
これに対し、比較例の No.14〜20は、製造条件が本発明規定外のため、いずれも引張強さまたは伸びが低く、従って成形性が劣った。
なお、No.15,16は中間焼鈍温度が適正でないため軟化率が本発明規定値を外れた。またNo.17,20は冷間圧延率が高かったため適正な調質焼鈍温度範囲が狭くなり、設定した調質焼鈍温度では伸びが十分回復せず成形性が不良となった。
【００３１】
【発明の効果】
以上に述べたように、本発明によれば、強度および伸びが高く成形性に優れるアルミニウム合金半硬質材を高歩留まりで製造できる。前記半硬質材は成形加工の自動化、高速化に十分対応でき、また張出し成形材、張出し部分の大きい複合成形材、エンボス加工材などにも適用できる。依って、工業上顕著な効果を奏する。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a method for producing an aluminum alloy semi-hard material excellent in formability with a high yield.
[0002]
[Prior art]
In general, there are two types of aluminum alloy semi-hard materials: an annealed tempered material obtained by annealing and softening a work hardened material and a processed tempered material obtained by work hardening of a fully annealed material. The former is H2X and the latter is H1X.
Since the annealed tempered material has a larger elongation and excellent formability than the processed tempered material, an annealed tempered material is usually used for press molding, and H24 having a relatively high strength is a typical semi-hard material. It is often used as.
The annealed tempered material is manufactured by subjecting an alloy ingot having a predetermined composition to homogenization, hot rolling, and cold rolling in this order, and annealing (tempering annealing) at a semi-softening temperature after the cold rolling. .
[0003]
[Problems to be solved by the invention]
Recently, with the progress of automation and speeding up of molding processes, semi-rigid materials are required to minimize fluctuations in quality and characteristics, and conventional semi-rigid materials cannot cope with the development of materials with better moldability. Improvement of the moldability limit is becoming essential.
[0004]
By the way, semi-rigid materials such as JIS-1100 and 1200 (all are low-strength materials) having a thickness of 0.5 to 2 mm, which are highly versatile as molding materials, are cold-rolled materials without intermediate annealing. It is manufactured by temper annealing.
However, since the cold-rolled material has an excessive cold work degree, softening occurs rapidly during temper annealing, and the annealing temperature range in which the required strength can be obtained is extremely narrow, and the temperature range also depends on the hot rolling conditions. Change. For this reason, there are many annealing defects such as insufficient annealing and over-annealing, and there is a problem that the manufacturing yield is lowered.
[0005]
On the other hand, cold-rolled materials with intermediate annealing are mildly softened during temper annealing, have a wide tempering annealing temperature range where the required strength can be obtained, and are less affected by hot rolling conditions. There are few. However, the annealed tempered material has a problem of low elongation and poor formability.
For these reasons, the present inventors have studied in detail the conditions such as ingot homogenization treatment, intermediate annealing, final cold rolling rate, temper annealing, etc. We have succeeded in finding a method for manufacturing with a high yield.
An object of the present invention is to produce an aluminum alloy semi-hard material (tempered annealing material) excellent in formability at a high yield.
[0006]
[Means for Solving the Problems]
The present invention contains Fe 0.2 to 0.9 wt%, Si 0.1 to 0.3 wt%, the ratio of the content of Fe and Si (Fe / Si) is 2.0 or more, the Fe and Si of The total content is 1.0 wt% or less, containing Cu 0.05 to 0.2 wt% as necessary, further Ti 0.005 to 0.05 wt%, B0.001 to 0.01 wt% % Or more, and the remainder is made of aluminum and inevitable impurities. The aluminum alloy ingot is homogenized, followed by hot rolling, cold rolling with intermediate annealing, and temper annealing in order. A method for producing an aluminum alloy semi-hard material to be applied, wherein the homogenization treatment is performed at a temperature of 540 to 610 ° C. for 1 to 15 hours, and at least final intermediate annealing is performed so that the softening rate is 20 to 70%, Perform cold rolling after intermediate annealing at a rolling rate of 50% or less. A manufacturing method of an aluminum alloy semi-rigid material which is excellent in formability, characterized in that applying a temper annealing at a temperature of 200 to 260 ° C..
[0007]
DETAILED DESCRIPTION OF THE INVENTION
The Al—Fe—Si alloy used in the present invention will be described.
Fe contributes to strength improvement and improves formability, and refines recrystallized grains by hot rolling or intermediate annealing to improve formability. Furthermore, it prevents skin roughness and improves the surface quality of the molded product.
The reason why the added amount of Fe is set to 0.2 to 0.9 wt% is that the effect cannot be sufficiently obtained when the amount is less than 0.2 wt%, and the effect is saturated when the amount exceeds 0.9 wt%. A coarse intermetallic compound is formed between the additive element or impurities, causing surface defects and detrimental to formability.
[0008]
Si dissolves in the Al matrix and contributes to strength improvement.
The reason why the Si content is specified to be 0.1 to 0.3 wt% is that the effect is not sufficiently obtained if the content is less than 0.1 wt%, and if it exceeds 0.3 wt%, a coarse intermetallic compound is formed with Fe. It is for producing | generating this and harming a moldability.
[0009]
Appropriate amounts of Fe and Si form an intermetallic compound together with Al to refine the recrystallized grains formed by hot rolling, intermediate annealing or the like, thereby improving formability. However, if the amount is too large, the intermetallic compound becomes coarse, the ductility is lowered, and the moldability is lowered. Therefore, the total content of Fe and Si is 1.0 wt% or less.
The amount of the intermetallic compound is also affected by the ratio of Fe and Si. That is, excess Si hinders the formation of the intermetallic compound, and thus hinders the formation of recrystallized nuclei, thereby coarsening the recrystallized grains. For this reason, the content ratio of Fe and Si (Fe / Si) is 2.0 or more, and the content ratio of Fe is increased.
[0010]
In the present invention, Cu is contained in the Al—Fe—Si alloy as necessary.
Cu improves strength and enhances formability. When anodized, the color tone is made uniform.
The reason why the Cu content is specified to be 0.05 to 0.2 wt% is that the effect cannot be sufficiently obtained when the content is less than 0.05 wt%, and the corrosion resistance decreases when the content exceeds 0.2 wt%.
[0011]
In the present invention, the Al—Fe—Si alloy contains one or two of Ti and B as required.
Ti refines the ingot structure to improve the rough surface of the rolled material and the non-uniformity of the appearance. The reason why the content is specified to be 0.005 to 0.05 wt% is that if the amount is less than 0.005 wt%, the effect cannot be sufficiently obtained. Intermetallic compounds are formed, which remain after rolling and cause surface scratches on the molded product, and also impair the moldability.
B promotes the refinement effect of Ti. If B is less than 0.001 wt%, the promoting effect cannot be sufficiently obtained. If it exceeds 0.01 wt%, a huge Ti-B intermetallic compound is produced during melt casting, which remains after rolling and is a molded product. Cause surface scratches.
In the present invention, even if the Cu and one or more of Ti or B coexist, each exhibits the same effect as described above.
[0012]
The semi-rigid material of the present invention is obtained by casting the aforementioned Al-Fe-Si- (Cu)-(Ti)-(B) alloy and cooling the resulting ingot with homogenization, hot rolling, and intermediate annealing. It is manufactured by performing intermediate rolling in order and finally tempering annealing.
By the homogenization treatment, segregation of solute elements in the ingot structure is homogenized, and the distribution of intermetallic compounds such as Fe and Si is optimized. In addition, the intermetallic compound is moderately coarsened by the homogenization treatment, and the moderately coarsened intermetallic compound functions effectively as a recrystallization nucleus in hot rolling and intermediate annealing, and forms a fine recrystallized structure. .
[0013]
The reason why the homogenization treatment is performed at a temperature of 540 to 610 ° C. for 1 to 15 hours is that the intermetallic compound is not coarsened appropriately at a temperature lower than 540 ° C. Therefore, the intermetallic compound that becomes a recrystallization nucleus is reduced and recycled. Crystal grains become coarse, formability and appearance are impaired, and when the temperature exceeds 610 ° C., the ingot is deformed or swollen, which later causes material defects. This is because if the homogenization time is less than 1 hour, the homogenization effect is not sufficiently obtained, and if it exceeds 15 hours, the effect is saturated and the cost becomes disadvantageous. A particularly desirable homogenization time is 2 to 6 hours.
[0014]
Hot rolling after the homogenization treatment is performed according to a conventional method. In the cold rolling after hot rolling, intermediate annealing is performed. As described above, the cold-rolled material with intermediate annealing can have a wide tempering annealing temperature range for obtaining the required strength.
Conventionally, this intermediate annealing was performed by complete annealing (complete recrystallization). However, in the case of complete annealing, if the cold rolling ratio before the intermediate annealing is not sufficiently increased, the re-annealing after the intermediate annealing is performed. Crystal grains become large and rough skin tends to occur.
For this reason, in the present invention, at least the final intermediate annealing is performed under the condition of partial recrystallization without complete recrystallization, that is, the condition that the softening rate is 20 to 70%.
[0015]
In the present invention, the reason why at least the final intermediate annealing is performed so that the softening rate is 20 to 70% is that if the softening rate is less than 20%, a large elongation that improves the moldability cannot be obtained after temper annealing. If it exceeds 70%, softening occurs rapidly during temper annealing, and defective annealing tends to occur, and a particularly desirable softening rate is 30 to 60%. Here, the softening rate is represented by the formula [(AB) / A]. However, A is the hardness of the material before intermediate annealing, and B is the hardness of the material after intermediate annealing.
[0016]
The crystal structure having a softening ratio of 20 to 70% is a mixture of fine recrystallized grains and non-recrystallized grains in which a subgrain boundary has developed.
The softening rate of 20 to 70% is obtained by intermediate annealing at a temperature of 220 to 280 ° C. That is, when the intermediate annealing temperature is less than 220 ° C., the sub-crystal grain boundaries of unrecrystallized grains do not develop sufficiently, and when it exceeds 280 ° C., it is difficult to control the softening rate to 20 to 70% by abrupt recrystallization. become.
[0017]
In the present invention, the reason why cold rolling after the final intermediate annealing is performed at a rolling rate of 50% or less is that when the rolling rate exceeds 50%, the elongation does not sufficiently recover after temper annealing, and the required formability is obtained. This is because there is not.
[0018]
In the present invention, the reason why the temper annealing is performed at a temperature of 200 to 260 ° C. is that if the temperature is less than 200 ° C., a large elongation that makes the moldability good cannot be obtained. This is because it gets worse.
[0019]
【Example】
Hereinafter, the present invention will be described in detail with reference to examples.
Example 1
An aluminum alloy ingot (thickness: 500 mm, width: 1200 mm, length: 4000 mm) having the composition defined in the present invention shown in Table 1 is subjected to homogenization treatment, hot rolling, intermediate annealing, and final cooling under the conditions of A shown in Table 2. Cold rolling and temper annealing were performed in order to produce a semi-rigid plate having a thickness of 1.0 mm. The homogenization time was 4 hours in all cases.
[0020]
(Comparative Example 1)
A semi-rigid plate having a thickness of 1.0 mm was manufactured in the same manner as in Example 1 except that an aluminum alloy ingot having a composition outside the scope of the present invention shown in Table 1 was used.
[0021]
About each semi-rigid board manufactured in Example 1 and Comparative Example 1, tensile strength, elongation, and moldability were investigated.
The formability was examined by an Erichsen test, and the punch moving distance (Erichsen value) until cracking in the rolled sheet was evaluated as poor (X) when it was less than 15 mm, and evaluated as good (◯) when it was 15 mm or more.
The results are shown in Table 3. Table 3 also shows the softening rate after the intermediate annealing.
[0022]
[Table 1]
[Table 2]
[Table 3]
As is apparent from Table 3, Nos. 1 to 3 of the examples of the present invention all have high tensile strength and elongation, and thus excellent moldability. Since intermediate annealing was performed during cold rolling, the temper annealing temperature range was widened and no annealing failure occurred.
On the other hand, Nos. 4 to 8 of the comparative examples were low in tensile strength and elongation because the alloy composition was outside the composition of the present invention, and therefore the formability was poor.
[0026]
(Example 2)
Using the aluminum alloy ingot having the composition No. 1 shown in Table 1, a semi-rigid plate having a thickness of 1.0 mm was manufactured under the manufacturing conditions B to E shown in Table 2.
[0027]
(Comparative Example 2)
Using an aluminum alloy ingot having the composition No. 1 shown in Table 1, a semi-rigid plate having a thickness of 1.0 mm was manufactured under the manufacturing conditions F to L shown in Table 2.
[0028]
About each semi-rigid board manufactured in Example 2 or Comparative Example 2, the tensile strength, elongation, and moldability were investigated by the same method as Example 1.
The results are shown in Table 4. Table 4 also shows the softening rate after the intermediate annealing.
[0029]
[Table 4]
As is apparent from Table 4, Nos. 9 to 13 of the examples of the present invention all had high tensile strength and elongation, and thus excellent moldability.
On the other hand, Nos. 14 to 20 of the comparative examples were low in tensile strength or elongation because the production conditions were outside the scope of the present invention, so that the moldability was inferior.
In Nos. 15 and 16, the softening rate deviated from the specified value of the present invention because the intermediate annealing temperature was not appropriate. In Nos. 17 and 20, since the cold rolling ratio was high, the appropriate temper annealing temperature range was narrowed, and the elongation was not sufficiently recovered at the set temper annealing temperature, resulting in poor formability.
[0031]
【The invention's effect】
As described above, according to the present invention, an aluminum alloy semi-hard material having high strength and elongation and excellent formability can be produced with a high yield. The semi-rigid material can sufficiently cope with automation and speeding up of the molding process, and can also be applied to a stretched molded material, a composite molded material having a large stretched portion, an embossed material, and the like. Therefore, there is an industrially significant effect.
Claims (4)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13659698A JP3857418B2 (en) | 1998-05-19 | 1998-05-19 | Method for producing aluminum alloy semi-hard material with excellent formability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13659698A JP3857418B2 (en) | 1998-05-19 | 1998-05-19 | Method for producing aluminum alloy semi-hard material with excellent formability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11323516A JPH11323516A (en) | 1999-11-26 |
| JP3857418B2 true JP3857418B2 (en) | 2006-12-13 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13659698A Expired - Fee Related JP3857418B2 (en) | 1998-05-19 | 1998-05-19 | Method for producing aluminum alloy semi-hard material with excellent formability |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP5291956B2 (en) * | 2008-03-10 | 2013-09-18 | 住友軽金属工業株式会社 | Aluminum alloy plate excellent in square tube deep drawing formability and manufacturing method thereof |
| JP4559513B2 (en) * | 2008-09-09 | 2010-10-06 | 株式会社神戸製鋼所 | Laminate and composite molded body |
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| JPH11323516A (en) | 1999-11-26 |
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