JP3853103B2 - Method for producing aluminum alloy sheet with excellent openability - Google Patents
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Description
【０００１】
【発明の属する技術分野】
本発明は果汁飲料及びコーヒー等の炭酸を含まない飲料の負圧缶に使用されるステイオンタブ式エンドに好適な開缶性が優れたアルミニウム合金板の製造方法に関し、特に、エンド成形後のレトルト処理又はエンド巻締め後の蓋内面の焼付塗装処理（以下、エンド巻締め後の蓋内面の焼付塗装処理をリペア処理という）等の熱処理を施された場合にも良好な開缶性を示す開缶性が優れたアルミニウム合金板の製造方法に関する。
【０００２】
【従来の技術】
近時、飲料等の缶の蓋には、地球環境問題の観点からステイオンタブ式エンドが急速に普及しているが、このエンドはリングプル式エンドとは開缶方法が相違しており、開缶に必要な力が大きく開けにくいため、スコア部の引裂き性の改善が重要な項目である。
【０００３】
また、ステイオンタブ式エンドを負圧缶に使用すると、負圧によりエンドの外形は凹状となる。この場合、外形が凸状となるビール等の炭酸を含む内容物が充填された容器と比して、開缶荷重が大きくなる傾向があることが本願発明者等の調査により判っている。負圧缶とは、果汁飲料及びコーヒー等の炭酸を含まない内容物が比較的高温で充填され、室内で缶内部が負の圧力を受ける缶である。
【０００４】
更に、負圧缶においては、エンド成形後に内容物充填後のレトルト処理又はリペア処理等により加熱されるので、開缶荷重が更に増加する傾向が認められる。
【０００５】
従来、負圧缶エンド材としては、ＪＩＳ Ａ５０５２等に規定される化学組成を有するアルミニウム合金鋳塊に熱間圧延及び冷間圧延を施した後、中間焼鈍を行い、更に、冷間圧延を施すことにより製造された材料が使用されている。しかし、ＪＩＳ Ａ５０５２合金を使用した場合には、開缶時に飲み口部をタブで押し下げ（ｐｏｐ）、更にスコア加工線に沿って引裂くｔｅａｒ（ティア）荷重が高く、亀裂の進展性が低いため、スコア部以外の部位にも亀裂が進み、飲み口全体が開口されない場合がある。
【０００６】
また、開缶時の荷重は材料の高強度化によって軽減されるものであり、ＪＩＳＡ５０５２合金の強度を向上させるためには冷間圧延率を増加させる必要があるが、この場合、合金中の結晶粒が扁平伸長粒となり、エンドの重要な特性の１つであるリベット加工性が低下してしまう。
【０００７】
一方、陽圧缶エンドに多く使用されているＪＩＳ Ａ５１８２合金では、ティア時の引裂き荷重を低減するために十分な強度を得ることが可能であるものの、ステイオンタブ式エンドは従来のエンドに比してスコア加工率が高いため、落下衝撃を受けた際にスコア割れの発生が著しくなる傾向がある。また、従来、負圧缶には３ピース缶用スチールボディが多く使用されており、このボディの衝撃吸収性が劣るため、エンド自体の衝撃吸収性を保持するためには著しい強度の向上は不利となる。
【０００８】
従来、キャンエンド材は、例えば、特開昭６３−２８６５４６号公報に記載された方法により製造されている。この従来の製造方法では、アルミニウム合金材に熱間圧延等を施し、更に冷間圧延を施して板厚を最終のものとした後、１００乃至２５０℃で仕上げ焼鈍として安定化処理を行うことにより、アルミニウム合金板の強度を調整している。
【０００９】
【課題を解決するための手段】
本発明に係る開缶性が優れたアルミニウム合金板の製造方法は、Ｍｇ：１．９０乃至３．００重量％、Ｍｎ：０．２０乃至０．７０重量％、Ｆｅ：０．１０乃至０．６０重量％及びＳｉ：０．０５乃至０．５０重量％と、を含有し、残部がＡｌ及び不可避的不純物からなる組成を有するアルミニウム合金鋳塊を均質化処理する工程と、前記アルミニウム合金鋳塊を熱間圧延する工程と、その後圧延率を８５乃至９５％としてタンデム圧延機により冷間圧延することにより、冷間圧延途中の中間焼鈍及び仕上げ焼鈍を施すことなく、板表面におけるＡｌ−Ｆｅ−Ｍｎ系晶出物の最大サイズを１乃至２０μｍ、Ａｌ−Ｆｅ−Ｍｎ系晶出物の面積占有率を０．５乃至１．５％、Ｍｇ−Ｓｉ系晶出物の最大サイズを１乃至２０μｍ、Ｍｇ−Ｓｉ系晶出物の面積占有率を０．１乃至１．０％とする工程とを有し、前記冷間圧延工程の終了温度が１１０乃至１４０℃であることを特徴とする。
【００１０】
そこで、化学組成が規定されたアルミニウム合金鋳塊から仕上げ焼鈍を施さずにアルミニウム合金板を製造する方法が提案されている（特開平６−３１６７３９号公報）。この従来の製造方法においては、アルミニウム合金鋳塊の化学組成を規定し、これに均質化熱処理、熱間圧延、圧延率３０％以上の冷間圧延及び中間焼鈍を施した後、再度冷間圧延を圧延率を３０乃至８０％として行っている。この方法によれば、所期の目的は達成できるものの、近時のより高い開缶性及び引裂き性に応えることは難しい。
【００１１】
本発明はかかる問題点に鑑みてなされたものであって、負圧缶ステイオンタブ式エンド材に必要とされるレトルト処理及びリペア処理等の加熱処理後の開缶性を向上させることができると共に、生産性を向上させることができる開缶性が優れたアルミニウム合金板の製造方法を提供することを目的とする。
【００１２】
【課題を解決するための手段】
本発明に係る開缶性が優れたアルミニウム合金板の製造方法は、Ｍｇ：１．９０乃至３．００重量％、Ｍｎ：０．２０乃至０．７０重量％、Ｆｅ：０．１０乃至０．６０重量％及びＳｉ：０．０５乃至０．５０重量％を含有し、残部がＡｌ及び不可避的不純物からなる組成を有するアルミニウム合金鋳塊を均質化処理する工程と、前記アルミニウム合金鋳塊を熱間圧延する工程と、その後圧延率を８５乃至９５％として冷間圧延することにより板表面におけるＡｌ−Ｆｅ−Ｍｎ系晶出物の最大サイズを１乃至２０μｍ、Ａｌ−Ｆｅ−Ｍｎ系晶出物の面積占有率を０．５乃至１．５％、Ｍｇ−Ｓｉ系晶出物の最大サイズを１乃至２０μｍ、Ｍｇ−Ｓｉ系晶出物の面積占有率を０．１乃至１．０％とする工程とを有し、前記冷間圧延工程の終了温度が１１０乃至１４０℃であることを特徴とする。
【００１３】
本発明においては、適切な組成を有するアルミニウム合金鋳塊を使用し、熱間圧延工程後の冷間圧延工程によりＡｌ−Ｆｅ−Ｍｎ系晶出物及びＭｇ−Ｓｉ系晶出物を適度に生成させることにより、開缶性を向上させている。これにより、負圧缶ステイオンタブ式エンドに使用され、レトルト処理及びリペア処理等の加熱処理を施された場合にも、十分な強度を保持したまま開缶荷重を低減することができる。また、冷間圧延工程の処理条件を適切に制御することにより、高生産性化及び低製造コスト化を実現することができる。
【００１４】
なお、本発明において、前記アルミニウム合金鋳塊は、Ｃｒ：０．１０乃至０．２５重量％、Ｃｕ：０．１０乃至０．２０重量％、Ｔｉ：０．０５乃至０．２０重量％及びＺｎ：０．０５乃至０．２０重量％からなる群から選択された少なくとも１種の元素を含有することが望ましい。これらの元素を含有することにより、強度又は開缶性が更に一層向上する。
【００１５】
また、前記冷間圧延工程にタンデム圧延機が使用されることが望ましい。
【００１６】
【発明の実施の形態】
本願発明者等が前記課題を解決するため、晶出物を増加させた場合の開缶性の向上に着目し、現有材料を使用してアルミニウム合金板の開缶性について鋭意実験研究を重ねた。そして、このように晶出物と開缶性との関係について調査した結果、アルミニウム合金板中に晶出物、特に、Ａｌ−Ｆｅ−Ｍｎ系晶出物及びＭｇ−Ｓｉ系晶出物が多いほど、ティア時の引裂き荷重が低くなって引裂き性及び開口性が向上すると共に、強度が向上して一定の変位量における引裂きの進展距離が長くなることを見出した。但し、晶出物の量が増加し材料強度が過剰になるほど、耐落下衝撃性が低下する傾向があるため、強度を著しく増加させることはできない。
【００１７】
更に、本願発明者等が鋭意研究を重ねた結果、アルミニウム合金鋳塊の化学組成を適正化して適切な径の晶出物を適度に分散させると共に、熱間圧延工程後の冷間圧延工程における圧延率及び終了温度を適切な範囲に制御することにより、比較的高強度でより開缶性及び引裂き性が優れたアルミニウム合金板を仕上げ焼鈍を施さなくても得ることができることに想到した。この場合、中間焼鈍を施す必要もないので、コストをより低減することもできる。
【００１８】
以下、本発明に使用されるアルミニウム合金鋳塊に含有される化学成分及びその組成限定理由について説明する。
【００１９】
Ｍｇ：１．９０乃至３．００重量％
Ｍｇは強度の向上及び開缶性の向上に寄与するＭｇーＳｉ系晶出物の生成のために重要な元素である。Ｍｇ含有量が１．９０重量％未満であると、負圧缶ステイオンタブ式エンド材としての十分な強度が得られない。一方、Ｍｇ含有量が３．００重量％を超えると、強度が高すぎることにより、落下時の衝撃によりスコア部に割れが生じる虞があると共に、成形性の低下を招く。従って、Ｍｇ含有量は１．９０乃至３．００重量％とする。
【００２０】
Ｍｎ：０．２０乃至０．７０重量％
Ｍｎはアルミニウム合金板の引裂き性を向上させるＡｌ−Ｆｅ−Ｍｎ系晶出物の生成及び強度の向上に大きな効果を有する元素である。Ｍｎ含有量が０．２０重量％未満であると、引裂き性の向上の効果が現れない。一方、Ｍｎ含有量が０．７０重量％を超えると、巨大晶出物が生成すると共に、晶出物の生成数が増加して、負圧缶ステイオンタブ式エンドとして使用される際の重要な特性である耐落下衝撃性及び成形性が低下する。従って、Ｍｎの含有量は０．２０乃至０．７０重量％とする。
【００２１】
Ｆｅ：０．１０乃至０．６０重量％
Ｆｅは開缶性を向上させるＡｌ−Ｆｅ−Ｍｎ系晶出物の生成に効果を有すると共に、エンドの成形性を向上させる結晶粒微細化に大きな効果を示す元素であり、その含有量が高いほど結晶粒微細化効果が高い。Ｆｅ含有量が０．１０重量％未満であると、結晶粒微細化及び開缶性の向上等の効果が不足する。一方、Ｆｅ含有量が０．６０重量％を超えると、巨大晶出物が生成されると共に、晶出物の生成数が過剰となり、負圧缶ステイオンタブ式エンドとして使用される際の重要な特性である耐落下衝撃性及び成形性が低下する。従って、Ｆｅの含有量は０．１０乃至０．６０重量％とする。
【００２２】
Ｓｉ：０．０５乃至０．５０重量％
Ｓｉは引裂き性を向上させるＭｇ−Ｓｉ系晶出物の生成に効果を示す元素である。Ｓｉ含有量が０．０５重量％未満であると、引裂き性向上の効果が得られない。一方、Ｓｉ含有量が０．５０重量％を超えると、巨大晶出物が生成されると共に、晶出物の生成数が過剰となり、成形性が低下する。従って、Ｓｉの含有量は０．０５乃至０．５０重量％とする。なお、より安定した開缶性及び成形性を得るためには、Ｓｉ含有量は０．１５乃至０．４０重量％であることが望ましい。
【００２３】
本発明においては、アルミニウム合金鋳塊に以下の元素が更に含有されていてもよい。
【００２４】
Ｃｒ：０．１０乃至０．２５重量％
Ｃｒはアルミニウム合金板の強度を向上させる効果を有する元素である。しかし、Ｃｒ含有量が０．１０重量％未満であると、強度向上の効果を得られない。一方、Ｃｒ含有量が０．２５重量％を超えると、巨大晶出物が生成されると共に、晶出物の生成数が多くなって成形性が低下しやすくなる。従って、Ｃｒの含有量は０．１０乃至０．２５重量％であることが望ましい。
【００２５】
Ｃｕ：０．１０乃至０．２０重量％
Ｃｕはアルミニウム合金板の強度を向上させる効果を有する元素である。しかし、Ｃｕ含有量が０．１０重量％未満であると、強度向上の効果が得られない。一方、Ｃｕ含有量が０．２０重量％を超えると、エンドとして使用される際の重要な特性である耐食性が低下しやすくなると共に、加工硬化が大きくなるため強度が高くなり過ぎて成形性が低下することがある。従って、Ｃｕの含有量は０．１０乃至０．２０重量％であることが望ましい。
【００２６】
Ｔｉ：０．０５乃至０．２０重量％
Ｔｉは組織の安定化に効果を有する元素である。しかし、Ｔｉ含有量が０．０５重量％未満であると、組織安定化の効果が得られない。一方、Ｔｉ含有量が０．２０重量％を超えると、巨大晶出物が生成されて成形性が低下しやすくなる。従って、Ｔｉの含有量は０．０５乃至０．２０重量％であることが望ましい。
【００２７】
Ｚｎ：０．０５乃至０．２０重量％
ＺｎはＡｌ−Ｆｅ−Ｍｎ系晶出物を微細化し、アルミニウム合金板の成形性を向上させる効果を有する元素である。しかし、Ｚｎ含有量が０．０５重量％未満であると、成形性向上の効果が得られない。一方、Ｚｎ含有量が０．２０重量％を超えても効果は少ない。従って、Ｚｎの含有量は０．０５乃至０．２０重量％であることが望ましい。
【００２８】
次に、本発明に係る開缶性が優れたアルミニウム合金板の製造方法について更に説明する。本発明においては、上述の組成を有するアルミニウム合金鋳塊に均質化処理（通常、４５０乃至５５０℃）を行い、更に熱間圧延（通常、開始温度が５００℃前後、終了温度が３００℃前後）及び冷間圧延を施して最終製品であるアルミニウム合金板を得る。以下に、冷間圧延工程における圧延条件の数値限定理由について説明する。
【００２９】
冷間圧延の圧延率：８５乃至９５％
冷間圧延の圧延率が８５％未満であると、負圧缶ステイオンタブ式エンド材に必要とされる強度を得ることができない。一方、冷間圧延の圧延率が９５％を超えると、アルミニウム合金板の強度が高くなり過ぎて成形性が低下すると共に、材料の異方性が増大する。従って、冷間圧延の圧延率は８５乃至９５％とする。
【００３０】
冷間圧延工程の発熱量及び圧延終了温度については、１回の圧延率と圧延速度である変形速度の影響が大きく、高速高圧下で圧延を行うほど生産性が向上する一方で、発熱量が増加し終了温度が高温となりアルミニウム合金の強度に影響を与える。
【００３１】
冷間圧延工程の終了温度：１１０乃至１４０℃
冷間圧延工程の終了温度が１１０℃未満であると、高強度化に対して有利であるものの、アルミニウム合金板の強度が高くなり過ぎて成形性が低下すると共に、仕上げ焼鈍が必要となる。更に、圧延速度と圧下率が著しく低下することに伴って生産性が著しく低下し、コストメリットがない。一方、終了温度が１４０℃を超えると、圧延速度の高速化と高圧下率化が可能となるものの、負圧缶ステイオンタブ式エンド材に必要とされる強度が不足すると共に、板表面の歪増加を招く。従って、冷間圧延工程の終了温度は１１０乃至１４０℃とする。
【００３２】
板表面におけるＡｌ−Ｆｅ−Ｍｎ系晶出物の最大サイズ：１乃至２０μｍ、面積占有率：０．５乃至１．５％
アルミニウム合金にＦｅ及びＭｎが含有されていると、（Ｆｅ、Ｍｎ）Ａｌ6等のＡｌ−Ｆｅ−Ｍｎ系晶出物が生成されるが、開缶性に寄与するのは最大サイズが１μｍ以上のものである。一方、最大サイズが２０μｍを超える巨大晶出物が生成されると成形性が低下する。従って、製造条件により晶出物の最大サイズを調整する必要がある。板表面におけるＡｌ−Ｆｅ−Ｍｎ系晶出物の面積占有率が０．５％未満であると、引裂き性及び開缶性向上の効果は得られず、面積占有率が１．５％を超えると、耐落下衝撃性及び成形性の低下が顕著になる。従って、板表面におけるＡｌ−Ｆｅ−Ｍｎ系晶出物の最大サイズは１乃至２０μｍ、Ａｌ−Ｆｅ−Ｍｎ系晶出物の面積占有率は０．５乃至１．５％とする。
【００３３】
板表面におけるＭｇ−Ｓｉ系晶出物の最大サイズ：１乃至２０μｍ、面積占有率：０．１乃至１．０％
アルミニウム合金にＳｉ及びＭｇが含有されていると、Ｍｇ2ＳｉのＭｇ−Ｓｉ系晶出物が生成されるが、開缶性に寄与するのは最大サイズが１μｍ以上のものである。一方、最大サイズが２０μｍを超える巨大晶出物が生成されると成形性が低下する。従って、素材であるアルミニウム合金鋳塊の化学組成及び製造条件により晶出物の最大サイズを調整する必要がある。板表面におけるＭｇ−Ｓｉ系晶出物の面積占有率が０．１％未満であると、開缶性及び引裂き性向上の効果は得られず、面積占有率が１．０％を超えると、耐落下衝撃性及び成形性の低下が顕著になる。従って、板表面におけるＭｇ−Ｓｉ系晶出物の最大サイズは１乃至２０μｍ、Ｍｇ−Ｓｉ系晶出物の面積占有率は０．１乃至１．０％とする。なお、より安定した開缶性及び成形性を得るためには、板表面における最大サイズが３乃至１５μｍのＡｌ−Ｆｅ−Ｍｎ系晶出物、Ｍｇ−Ｓｉ系晶出物の面積占有率は夫々０．８乃至１．２％、０．３乃至０．７％であることが望ましい。
【００３４】
なお、冷間圧延工程ではタンデム圧延機を使用することが望ましい。タンデム圧延機を使用することにより、シングルの圧延機と比して、１回の通板における圧延率を高くすることができる。これにより、１回の通板における発熱量が安定して高くなるので、従来のように冷間圧延後に仕上げ焼鈍を施す場合と比して効率よくアルミニウム合金板を製造することができる。
【００３５】
また、冷間圧延後に仕上げ焼鈍を施してもよい。
【００３６】
【実施例】
以下、本発明の実施例について、その特許請求の範囲から外れる比較例と比較して具体的に説明する。
【００３７】
第１の実施例
先ず、下記表１に示す化学組成を有するアルミニウム合金鋳塊を５１０℃で４時間均質化熱処理した後、熱間圧延により板厚が２．５ｍｍの圧延板とした。３５０℃で２４時間の焼鈍後、タンデム冷間圧延機にて終了温度が１３０℃となる冷間圧延を行うことにより、圧延板の板厚を０．２３ｍｍとした。なお、比較例１８はＪＩＳ Ａ５０５２合金であり、比較例１９はＪＩＳ Ａ５１８２合金である。
【００３８】
【表１】
通常、エンド材は塗装後成形加工されるので、冷間圧延後のアルミニウム合金板に２８５℃で２０秒間の塗装焼付相当の熱処理（ベーキング処理）を施した。そして、その表面における最大サイズが１乃至２０μｍのＡｌ−Ｆｅ−Ｍｎ系晶出物の占有面積率及び最大サイズが１乃至２０μｍのＭｇ−Ｓｉ系晶出物の占有面積率を測定した。また、機械的性質として、引張強さ、耐力及び伸びを測定した。これらの結果を下記表２に示す。
【００４０】
【表２】
更に、各アルミニウム合金板をステイオンタブ式エンドに加工した後、開缶性、耐落下衝撃性及びリベット張出し限界の評価を行った。
【００４２】
開缶性の評価においては、先ず、ステイオンタブ式エンドに加工されたアルミニウム合金板をキャンボディに巻き締めた。図１は開缶性の試験方法を示す模式図である。巻き締め後、図１に示すように、エンド１を回転中心としてボディ２を回転させて開缶に要する荷重を検出器３により測定した。そして、開缶荷重が２４Ｎ未満であるものを良好、２４Ｎ以上であるものを不良と判断した。
【００４３】
また、耐落下衝撃性の評価においては、先ず、９０℃の湯を缶に充填し巻き締めを行い、放冷し負圧缶の状態とした。図２は耐落下衝撃性の試験方法を示す模式図である。巻き締め後、４００ｍｍの高さからエンド１１を下側にして缶１２をパイプ１３中を垂直に鉄板１４に落下させ、スコアに割れが生じるまでの回数を測定した。そして、平均回数が４回を超えるものを良好、４回以下であるものを不良と判断した。
【００４４】
リベット張出し限界の評価においては、直径を順に６ｍｍ、４ｍｍ、３．２ｍｍとする張出し絞り加工を行った。そして、張出し限界高さが１．７０ｍｍを超えるものを良好、１．７０ｍｍ以下であるものを不良と判断した。
【００４５】
これらの結果を下記表３に示す。なお、表３の開缶荷重の欄において、ポップ（ｐｏｐ）とは開缶初期時の開缶荷重であり、ティアとはスコアに沿ってタブで押し込む時の開缶荷重である。
【００４６】
【表３】
上記表３に示すように、実施例１乃至８においては、適切な組成を有するアルミニウム合金鋳塊に適切な処理を施してアルミニウム合金板としたので、開缶荷重が低く開缶性が優れていた。また、耐落下衝撃性も優れており、エンド材に必要な特性であるリベット張出し成形性も十分に高かった。
【００４８】
比較例１０においては、Ｍｇ含有量が本発明範囲の下限未満（強度が低い）であるため、比較例１２においては、Ｍｎ含有量が本発明範囲の下限未満であるため、比較例１４においては、Ｆｅ含有量が本発明範囲の下限未満であるため、比較例１６においては、Ｓｉ含有量が本発明範囲の下限未満であるため、開缶性の向上に寄与するＡｌ−Ｆｅ−Ｍｎ系晶出物又はＭｇ−Ｓｉ系晶出物の占有面積率が本発明範囲の下限未満となって、開缶荷重が高くなった。
【００４９】
比較例１１においては、Ｍｇ含有量が本発明範囲の上限を超えているため、比較例１３においては、Ｍｎ含有量が本発明範囲の上限を超えているため、比較例１５においては、Ｆｅ含有量が本発明範囲の上限を超えているため、比較例９及び１７においては、Ｓｉ含有量が本発明範囲の上限を超えているため、Ａｌ−Ｆｅ−Ｍｎ系晶出物又はＭｇ−Ｓｉ系晶出物の占有面積率が本発明範囲の上限を超え、耐落下衝撃性が劣っていた。更に、リベット限界高さが低かった。
【００５０】
比較例１８はＪＩＳ ５０５２合金であり、Ｍｎが含有されていないので、Ａｌ−Ｆｅ−Ｍｎ系晶出物の占有面積率が極めて低く、ホップ時の開缶荷重が高い。
【００５１】
比較例１９は、ＪＩＳ Ａ５１８２アルミニウム合金であり、高い強度が得られるものの、耐落下衝撃性が劣る。また、Ａｌ−Ｆｅ−Ｍｎ系晶出物とＭｇ−Ｓｉ系晶出物の占有面積率が比較的低いため、ポップ時の開缶荷重が高い。
【００５２】
第２の実施例
先ず、上記表１の実施例８に示す化学組成を有するアルミニウム合金鋳塊を、第１の実施例同様に、５１０℃で４時間均質化熱処理した後、熱間圧延により板厚が２．５ｍｍの圧延板とした。次に、表４に示すように、実施例２１及び２２並びに比較例２６及び２７においては、板厚１．６４ｍｍまで冷間圧延し、比較例２８乃至３０においては、板厚０．９２ｍｍまで圧延し、連続焼鈍（ＣＡＬ）を施した。その後、下記表４に示す条件で各圧延板に冷間圧延を行った。また、実施例２０及び比較例２３乃至２５においては、表４に示すように、連続焼鈍を行わずに２．５ｍｍの圧延板を冷間圧延により所定の板厚とした。比較例２３以外における板厚は、全て０．２３ｍｍである。また、表４には、圧延率、温度及びパス数を示す。
【００５３】
【表４】
そして、第１の実施例と同様にして、機械的性質、開缶荷重、耐落下衝撃性及びリベット張出し限界の評価を行った。
【００５５】
また、工程上、焼鈍の有無及び圧延回数等の観点から生産性及び製造コストの評価を行った。これらの結果を下記表５に示す。実施例に関しては、タンデム圧延を行い、比較例ではシングル圧延を行った。◎は良好であることを示し、○はやや良であることを示し、△はやや不良であることを示し、×は不良であることを示している。
【００５６】
【表５】
【表６】
上記表５及び６に示すように、実施例２０乃至２２においては、適切な組成を有するアルミニウム合金鋳塊に適切な冷間圧延を施してアルミニウム合金板としたので、良好な機械的性質及び引裂き性が得られた。更に、高生産性化及び低製造コスト化が可能であった。
【００５９】
一方、比較例２３においては、板厚が薄すぎるため評価はできないが、強度が高いことにより、耐落下衝撃性及びリベット張出し限界高さが劣っていることが予測される。比較例２８乃至３０においては、冷間圧延率が本発明範囲の下限未満であるので、負圧缶ステイオンタブ式エンド材に必要とされる強度が得られないと共に、開缶荷重が高い。
【００６０】
比較例２４及び２６においては、冷間圧延工程の終了温度が本発明範囲の下限未満なので、ややリベット張出し性が劣るものの、他の特性は良好である。但し、高速の冷間圧延が困難となるので、生産性が本発明の約半分であり、製造コストが本発明の約１．３倍となる。比較例２５及び２７においては、冷間圧延工程の終了温度が本発明範囲の上限を超えているので、生産性及び製造コストの他に、ポップ時の開缶荷重が高く、負圧缶ステイオンタブ式エンド材には不足である。
【００６１】
【発明の効果】
以上詳述したように、本発明によれば、適切な組成を有するアルミニウム合金鋳塊を使用し、熱間圧延工程後の冷間圧延工程によりＡｌ−Ｆｅ−Ｍｎ系晶出物及びＭｇ−Ｓｉ系晶出物を適度に生成させているので、十分な強度を保持したまま開缶荷重を低減することができる。これにより、果汁飲料及びコーヒー等の炭酸を含まない飲料の缶等に使用される負圧缶ステイオンタブ式エンド材としてレトルト処理及びリペア処理等の熱処理後の開缶時の荷重が低く、エンド特性を十分に満足することができると共に、高生産性化及び低製造コスト化が可能であり、薄肉高強度化にも十分適応することができる。また、冷間圧延工程時にタンデム圧延機を使用することにより、より生産性を向上させることができる。
【図面の簡単な説明】
【図１】開缶性の試験方法を示す模式図である。
【図２】図２は耐落下衝撃性の試験方法を示す模式図である。
【符号の説明】
１、１１；エンド
２；ボディ
３；検出器
１２；缶
１３；パイプ
１４；鉄板[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a method for producing an aluminum alloy plate excellent in can openability suitable for a steion tab type end used for a negative pressure can of fruit juice beverages and beverages not containing carbonic acid such as coffee, and in particular, after end molding Excellent openability even when heat treatment such as retort treatment or baking finish treatment on the inner surface of the lid after end winding (hereinafter referred to as repair treatment) The present invention relates to a method for producing an aluminum alloy plate having excellent openability.
[0002]
[Prior art]
Recently, a steion tub type end is rapidly spreading in the lids of cans for beverages and the like from the viewpoint of global environmental problems, but this end is different from the ring-pull type end in the method of opening the can. Since the force required for the can is large and difficult to open, improving the tearability of the score part is an important item.
[0003]
Moreover, when a steion tab type end is used for a negative pressure can, the external shape of the end becomes concave due to the negative pressure. In this case, the inventors of the present application have found that the opening load tends to increase as compared with a container filled with carbon dioxide-containing contents such as beer whose outer shape is convex. The negative pressure can is a can filled with a content not containing carbonic acid such as a fruit juice drink and coffee at a relatively high temperature, and the inside of the can receives a negative pressure inside the room.
[0004]
Furthermore, since the negative pressure can is heated by retorting or repair after filling the contents after end molding, a tendency to further increase the opening load can be recognized.
[0005]
Conventionally, as a negative pressure can end material, after hot rolling and cold rolling are performed on an aluminum alloy ingot having a chemical composition defined in JIS A5052, etc., intermediate annealing is performed, and further cold rolling is performed. The material produced by this is used. However, when JIS A5052 alloy is used, the tear opening is pushed down with a tab when opening the can (pop), and the tear load along the score processing line is high, and crack progress is low. In some cases, cracks also progress in parts other than the score part, and the entire drinking mouth is not opened.
[0006]
Moreover, the load at the time of opening the can is reduced by increasing the strength of the material, and in order to improve the strength of the JIS A5052 alloy, it is necessary to increase the cold rolling rate. The grains become flat elongated grains, and the rivet processability, which is one of the important characteristics of the end, is lowered.
[0007]
On the other hand, with JIS A5182 alloy, which is often used for positive pressure can ends, it is possible to obtain sufficient strength to reduce the tearing load at the time of tearing. Since the score processing rate is high, the score cracking tends to be remarkable when subjected to a drop impact. Conventionally, a steel body for a three-piece can has been used in many negative pressure cans, and the shock absorption of this body is inferior, so a significant improvement in strength is disadvantageous in order to maintain the shock absorption of the end itself. It becomes.
[0008]
Conventionally, can-end materials are manufactured by the method described in Japanese Patent Laid-Open No. 63-286546, for example. In this conventional manufacturing method, the aluminum alloy material is subjected to hot rolling or the like, further subjected to cold rolling to obtain a final thickness, and then subjected to stabilization treatment as finish annealing at 100 to 250 ° C. The strength of the aluminum alloy plate is adjusted.
[0009]
[Means for Solving the Problems]
The manufacturing method of the aluminum alloy plate excellent in can opening property according to the present invention is Mg: 1.90 to 3.00 wt%, Mn: 0.20 to 0.70 wt%, Fe: 0.10 to 0.00. A step of homogenizing an aluminum alloy ingot containing 60% by weight and Si: 0.05 to 0.50% by weight, the balance being composed of Al and inevitable impurities, and the aluminum alloy ingot And then rolling the sheet at a rolling rate of 85 to 95% with a tandem rolling mill, without subjecting the intermediate and finish annealing during the cold rolling to Al-Fe- on the plate surface. The maximum size of the Mn-based crystallized product is 1 to 20 μm, the area occupation ratio of the Al—Fe—Mn-based crystallized product is 0.5 to 1.5%, and the maximum size of the Mg—Si-based crystallized product is 1 to 20 μm. , Mg-Si crystallized product And an area occupancy ratio of 0.1 to 1.0%, and the end temperature of the cold rolling process is 110 to 140 ° C.
[0010]
In view of this, there has been proposed a method for producing an aluminum alloy plate from an aluminum alloy ingot having a prescribed chemical composition without subjecting it to finish annealing (Japanese Patent Laid-Open No. 6-316739). In this conventional manufacturing method, the chemical composition of the aluminum alloy ingot is defined, and after this, it is subjected to homogenization heat treatment, hot rolling, cold rolling with a rolling rate of 30% or more and intermediate annealing, and then cold rolling again. The rolling rate is 30 to 80%. According to this method, although the intended purpose can be achieved, it is difficult to meet the recent higher can openability and tearability.
[0011]
This invention is made | formed in view of this problem, Comprising: The openability after heat processing, such as a retort process and a repair process required for a negative pressure can steon tub type end material, can be improved. At the same time, it is an object of the present invention to provide a method for producing an aluminum alloy plate excellent in can openability that can improve productivity.
[0012]
[Means for Solving the Problems]
The manufacturing method of the aluminum alloy plate excellent in can opening property according to the present invention is Mg: 1.90 to 3.00 wt%, Mn: 0.20 to 0.70 wt%, Fe: 0.10 to 0.00. A step of homogenizing an aluminum alloy ingot containing 60% by weight and Si: 0.05 to 0.50% by weight, the balance being composed of Al and inevitable impurities; and heating the aluminum alloy ingot The maximum size of the Al—Fe—Mn based crystallized material on the surface of the plate is 1 to 20 μm, and the Al—Fe—Mn based crystallized product is obtained by cold rolling at a rolling rate of 85 to 95%. Area occupancy of 0.5 to 1.5%, the maximum size of Mg-Si based crystals is 1 to 20 μm, and the area occupation rate of Mg-Si based crystals is 0.1 to 1.0%. And an end temperature of the cold rolling step Is 110 to 140 ° C.
[0013]
In the present invention, an aluminum alloy ingot having an appropriate composition is used, and an Al—Fe—Mn based crystallized product and an Mg—Si based crystallized product are appropriately generated by the cold rolling process after the hot rolling process. By making it, the can opening property is improved. Thereby, even when it is used for a negative pressure can steion tab type end and subjected to heat treatment such as retort treatment and repair treatment, the can opening load can be reduced while maintaining sufficient strength. In addition, high productivity and low manufacturing cost can be realized by appropriately controlling the processing conditions of the cold rolling process.
[0014]
In the present invention, the aluminum alloy ingot is composed of Cr: 0.10 to 0.25% by weight, Cu: 0.10 to 0.20% by weight, Ti: 0.05 to 0.20% by weight, and Zn. It is desirable to contain at least one element selected from the group consisting of 0.05 to 0.20% by weight. By containing these elements, the strength or openability is further improved.
[0015]
Moreover, it is desirable that a tandem rolling mill is used for the cold rolling process.
[0016]
DETAILED DESCRIPTION OF THE INVENTION
In order to solve the above-mentioned problems, the inventors of the present application focused on improving the can openability when increasing the amount of crystallized materials, and conducted extensive experimental research on the can openability of aluminum alloy plates using existing materials. . And as a result of investigating the relationship between the crystallized product and the openability as described above, there are many crystallized products in the aluminum alloy plate, in particular, Al-Fe-Mn based crystallized products and Mg-Si based crystallized products. It has been found that the tearing load at the time of tearing is lowered to improve the tearability and openability, and the strength is improved to increase the tear propagation distance at a certain amount of displacement. However, since the drop impact resistance tends to decrease as the amount of crystallized material increases and the material strength becomes excessive, the strength cannot be significantly increased.
[0017]
Furthermore, as a result of repeated extensive research by the inventors of the present application, the chemical composition of the aluminum alloy ingot is optimized to appropriately disperse the crystallized material having an appropriate diameter, and in the cold rolling process after the hot rolling process. It was conceived that by controlling the rolling rate and the end temperature within an appropriate range, it is possible to obtain an aluminum alloy sheet having a relatively high strength and excellent can openability and tearability without performing finish annealing. In this case, since it is not necessary to perform intermediate annealing, the cost can be further reduced.
[0018]
Hereinafter, the chemical components contained in the aluminum alloy ingot used in the present invention and the reasons for limiting the composition will be described.
[0019]
Mg: 1.90 to 3.00% by weight
Mg is an important element for the production of Mg-Si-based crystallized substances that contribute to the improvement of strength and the improvement of can openability. If the Mg content is less than 1.90% by weight, sufficient strength as a negative pressure can steion tab type end material cannot be obtained. On the other hand, if the Mg content exceeds 3.00% by weight, the strength is too high, so that there is a possibility that the score part will be cracked by the impact at the time of dropping, and the moldability is lowered. Therefore, the Mg content is 1.90 to 3.00% by weight.
[0020]
Mn: 0.20 to 0.70% by weight
Mn is an element that has a great effect on the formation of Al-Fe-Mn crystallized substances that improve the tearability of the aluminum alloy sheet and the improvement of strength. When the Mn content is less than 0.20% by weight, the effect of improving tearability does not appear. On the other hand, when the Mn content exceeds 0.70% by weight, a large crystallized product is generated, and the number of crystallized products is increased, which is important when used as a negative pressure can steion tab type end. The drop impact resistance and moldability, which are special characteristics, are reduced. Therefore, the Mn content is 0.20 to 0.70% by weight.
[0021]
Fe: 0.10 to 0.60% by weight
Fe is an element that has an effect on the formation of Al-Fe-Mn-based crystallized substances that improve can openability, and has a great effect on crystal grain refinement that improves end moldability, and its content is high. The crystal grain refinement effect is higher. When the Fe content is less than 0.10% by weight, effects such as refinement of crystal grains and improvement of openability are insufficient. On the other hand, when the Fe content exceeds 0.60% by weight, a large amount of crystallized material is generated and the number of crystallized products is excessive, which is important when used as a negative pressure can steion tab type end. The drop impact resistance and moldability, which are special characteristics, are reduced. Therefore, the Fe content is set to 0.10 to 0.60% by weight.
[0022]
Si: 0.05 to 0.50% by weight
Si is an element that has an effect on the formation of Mg-Si based crystallized substances that improve tearability. If the Si content is less than 0.05% by weight, the effect of improving tearability cannot be obtained. On the other hand, when the Si content exceeds 0.50% by weight, a large crystallized product is generated, and the number of crystallized products generated becomes excessive, resulting in a decrease in moldability. Therefore, the Si content is 0.05 to 0.50% by weight. In order to obtain more stable can openability and moldability, the Si content is desirably 0.15 to 0.40% by weight.
[0023]
In the present invention, the aluminum alloy ingot may further contain the following elements.
[0024]
Cr: 0.10 to 0.25% by weight
Cr is an element having an effect of improving the strength of the aluminum alloy plate. However, if the Cr content is less than 0.10% by weight, the effect of improving the strength cannot be obtained. On the other hand, when the Cr content exceeds 0.25% by weight, a large crystallized product is generated, and the number of crystallized products generated increases, and the formability tends to decrease. Accordingly, the Cr content is desirably 0.10 to 0.25% by weight.
[0025]
Cu: 0.10 to 0.20% by weight
Cu is an element having an effect of improving the strength of the aluminum alloy plate. However, if the Cu content is less than 0.10% by weight, the effect of improving the strength cannot be obtained. On the other hand, if the Cu content exceeds 0.20% by weight, the corrosion resistance, which is an important characteristic when used as an end, tends to decrease, and the work hardening increases, so the strength becomes too high and the moldability becomes high. May decrease. Accordingly, the Cu content is desirably 0.10 to 0.20% by weight.
[0026]
Ti: 0.05 to 0.20% by weight
Ti is an element having an effect on the stabilization of the structure. However, if the Ti content is less than 0.05% by weight, the effect of stabilizing the structure cannot be obtained. On the other hand, when the Ti content exceeds 0.20% by weight, a giant crystallized product is generated and the moldability tends to be lowered. Therefore, the Ti content is desirably 0.05 to 0.20% by weight.
[0027]
Zn: 0.05 to 0.20% by weight
Zn is an element having the effect of refining the Al—Fe—Mn-based crystallized substance and improving the formability of the aluminum alloy plate. However, if the Zn content is less than 0.05% by weight, the effect of improving moldability cannot be obtained. On the other hand, the effect is small even if the Zn content exceeds 0.20% by weight. Accordingly, the Zn content is desirably 0.05 to 0.20% by weight.
[0028]
Next, the manufacturing method of the aluminum alloy plate excellent in can opening property according to the present invention will be further described. In the present invention, the aluminum alloy ingot having the above composition is subjected to a homogenization treatment (usually 450 to 550 ° C.), and further hot-rolled (usually a start temperature of around 500 ° C. and an end temperature of around 300 ° C.). And it cold-rolls and the aluminum alloy plate which is a final product is obtained. The reason for limiting the numerical values of the rolling conditions in the cold rolling process will be described below.
[0029]
Cold rolling reduction ratio: 85 to 95%
When the rolling rate of the cold rolling is less than 85%, it is not possible to obtain the strength required for the negative pressure canned steion tab type end material. On the other hand, when the rolling rate of cold rolling exceeds 95%, the strength of the aluminum alloy plate becomes too high, the formability is lowered, and the anisotropy of the material is increased. Therefore, the rolling rate of cold rolling is 85 to 95%.
[0030]
About the calorific value and rolling end temperature of the cold rolling process, the influence of the deformation rate which is the rolling rate and rolling speed is large, and the productivity increases as the rolling is performed under high speed and high pressure, while the calorific value is It increases and the end temperature becomes high, affecting the strength of the aluminum alloy.
[0031]
End temperature of the cold rolling process: 110 to 140 ° C.
If the end temperature of the cold rolling process is less than 110 ° C., it is advantageous for increasing the strength, but the strength of the aluminum alloy sheet becomes too high, the formability is lowered, and finish annealing is required. Furthermore, the productivity is remarkably reduced as the rolling speed and rolling reduction are remarkably reduced, and there is no cost merit. On the other hand, if the end temperature exceeds 140 ° C., the rolling speed can be increased and the high-pressure reduction rate can be achieved, but the strength required for the negative pressure canister stabbed end material is insufficient, and the plate surface Increases distortion. Accordingly, the end temperature of the cold rolling process is set to 110 to 140 ° C.
[0032]
Maximum size of Al—Fe—Mn crystallized material on the plate surface: 1 to 20 μm, area occupancy: 0.5 to 1.5%
When the aluminum alloy contains Fe and Mn, an Al—Fe—Mn crystallized product such as (Fe, Mn) Al 6 is generated, but the maximum size is 1 μm or more which contributes to the openability. belongs to. On the other hand, if a large crystallized product having a maximum size exceeding 20 μm is produced, the moldability is lowered. Therefore, it is necessary to adjust the maximum size of the crystallized product according to the production conditions. When the area occupancy of the Al—Fe—Mn crystallized material on the plate surface is less than 0.5%, the effect of improving tearability and can openability cannot be obtained, and the area occupancy exceeds 1.5%. And drop impact resistance and a fall of a moldability become remarkable. Therefore, the maximum size of the Al—Fe—Mn crystallized material on the plate surface is 1 to 20 μm, and the area occupation ratio of the Al—Fe—Mn crystallized material is 0.5 to 1.5%.
[0033]
Maximum size of Mg—Si based crystallized material on the plate surface: 1 to 20 μm, area occupancy: 0.1 to 1.0%
When Si and Mg are contained in the aluminum alloy, Mg 2 Si crystallized crystals of Mg 2 Si are generated, but the maximum size contributes to the can opening property when the maximum size is 1 μm or more. On the other hand, if a large crystallized product having a maximum size exceeding 20 μm is produced, the moldability is lowered. Therefore, it is necessary to adjust the maximum size of the crystallized product according to the chemical composition and production conditions of the aluminum alloy ingot as a raw material. If the area occupancy of the Mg-Si-based crystallized material on the plate surface is less than 0.1%, the effect of improving the openability and tearability cannot be obtained, and if the area occupancy exceeds 1.0%, The drop impact resistance and moldability are significantly reduced. Therefore, the maximum size of the Mg—Si based crystallized material on the plate surface is 1 to 20 μm, and the area occupation ratio of the Mg—Si based crystallized material is 0.1 to 1.0%. In order to obtain more stable can openability and formability, the area occupancy of the Al—Fe—Mn crystallized product and the Mg—Si crystallized product having a maximum size of 3 to 15 μm on the plate surface is respectively set. It is desirable to be 0.8 to 1.2% and 0.3 to 0.7%.
[0034]
In the cold rolling process, it is desirable to use a tandem rolling mill. By using a tandem rolling mill, it is possible to increase the rolling rate in a single sheet pass as compared with a single rolling mill. Thereby, since the calorific value in one pass sheet becomes high stably, an aluminum alloy sheet can be manufactured more efficiently compared with the case where finish annealing is performed after cold rolling as in the prior art .
[0035]
Moreover, you may give finish annealing after cold rolling.
[0036]
【Example】
Examples of the present invention will be specifically described below in comparison with comparative examples that depart from the scope of the claims.
[0037]
First Example First, an aluminum alloy ingot having the chemical composition shown in Table 1 below was subjected to homogenization heat treatment at 510C for 4 hours, and then rolled into a rolled plate having a thickness of 2.5 mm by hot rolling. did. After annealing at 350 ° C. for 24 hours, cold rolling was performed at a finish temperature of 130 ° C. with a tandem cold rolling mill, so that the thickness of the rolled plate was 0.23 mm. Comparative Example 18 is a JIS A5052 alloy, and Comparative Example 19 is a JIS A5182 alloy.
[0038]
[Table 1]
Usually, since the end material is formed and processed after coating, the cold-rolled aluminum alloy plate was subjected to heat treatment (baking treatment) corresponding to coating baking at 285 ° C. for 20 seconds. And the occupation area rate of the Al-Fe-Mn type | system | group crystallized material whose maximum size is 1 thru | or 20 micrometers in the surface, and the occupation area rate of the Mg-Si type | system | group crystallized material whose maximum size is 1 thru | or 20 micrometers were measured. Moreover, tensile strength, proof stress, and elongation were measured as mechanical properties. These results are shown in Table 2 below.
[0040]
[Table 2]
Further, after each aluminum alloy plate was processed into a steion tab type end, the can openability, the drop impact resistance and the rivet overhang limit were evaluated.
[0042]
In the evaluation of can openability, first, an aluminum alloy plate processed into a steion tab type end was wound around a can body. FIG. 1 is a schematic view showing a can openability test method. After the tightening, as shown in FIG. 1, the load required to open the can was measured by rotating the
[0043]
Further, in the evaluation of the drop impact resistance, first, the can was filled with 90 ° C. hot water, and the can was cooled and allowed to cool to a negative pressure can. FIG. 2 is a schematic view showing a drop impact resistance test method. After winding, the can 12 was dropped from the height of 400 mm onto the iron plate 14 vertically with the end 11 facing downward, and the number of times until the score was cracked was measured. And the average number of times exceeding 4 times was judged as good, and the number of times less than 4 was judged as bad.
[0044]
In the evaluation of the rivet overhang limit, overdrawing drawing was performed in which the diameters were sequentially 6 mm, 4 mm, and 3.2 mm. And what overhang limit height exceeded 1.70 mm was judged favorable, and the thing which is 1.70 mm or less was judged to be bad.
[0045]
These results are shown in Table 3 below. In the column of can open load in Table 3, the pop is the open load at the initial stage of the open can, and the tier is the open load when the tab is pushed in along the score.
[0046]
[Table 3]
As shown in Table 3 above, in Examples 1 to 8, since the aluminum alloy ingot having an appropriate composition was appropriately treated to form an aluminum alloy plate, the can open load was low and the can openability was excellent. It was. Moreover, the drop impact resistance was excellent, and the rivet stretch formability, which is a characteristic required for the end material, was sufficiently high.
[0048]
In Comparative Example 10, the Mg content is less than the lower limit of the present invention range (low strength). Therefore, in Comparative Example 12, the Mn content is less than the lower limit of the present invention range. In Comparative Example 16, since the Fe content is less than the lower limit of the range of the present invention, the Si content is less than the lower limit of the range of the present invention. The occupied area ratio of the extract or the Mg-Si-based crystallized product became less than the lower limit of the range of the present invention, and the can opening load was increased.
[0049]
In Comparative Example 11, since the Mg content exceeds the upper limit of the range of the present invention, in Comparative Example 13, the Mn content exceeds the upper limit of the range of the present invention. Since the amount exceeds the upper limit of the range of the present invention, in Comparative Examples 9 and 17, since the Si content exceeds the upper limit of the range of the present invention, Al-Fe-Mn-based crystallized product or Mg-Si-based The occupied area ratio of the crystallized product exceeded the upper limit of the range of the present invention, and the drop impact resistance was inferior. Furthermore, the rivet limit height was low.
[0050]
Since the comparative example 18 is a JIS 5052 alloy and does not contain Mn, the occupied area rate of the Al-Fe-Mn based crystallized substance is extremely low, and the opening load at the time of hop is high.
[0051]
Comparative Example 19 is a JIS A5182 aluminum alloy, which has high strength but is inferior in drop impact resistance. Moreover, since the occupied area ratio of the Al—Fe—Mn crystallized product and the Mg—Si based crystallized product is relatively low, the opening load during popping is high.
[0052]
Second example First, an aluminum alloy ingot having the chemical composition shown in Example 8 in Table 1 is subjected to a homogenization heat treatment at 510C for 4 hours in the same manner as in the first example. A rolled plate having a thickness of 2.5 mm was obtained by hot rolling. Next, as shown in Table 4, in Examples 21 and 22 and Comparative Examples 26 and 27, cold rolling was performed to a plate thickness of 1.64 mm, and in Comparative Examples 28 to 30, rolling was performed to a plate thickness of 0.92 mm. Then, continuous annealing (CAL) was performed. Thereafter, each rolled sheet was cold-rolled under the conditions shown in Table 4 below. Moreover, in Example 20 and Comparative Examples 23 to 25, as shown in Table 4, a 2.5 mm rolled plate was made into a predetermined plate thickness by cold rolling without performing continuous annealing. The plate thicknesses other than Comparative Example 23 are all 0.23 mm. Table 4 shows the rolling rate, temperature, and number of passes.
[0053]
[Table 4]
In the same manner as in the first example, the mechanical properties, can open load, drop impact resistance, and rivet overhang limit were evaluated.
[0055]
Moreover, productivity and manufacturing cost were evaluated from the viewpoints of the presence or absence of annealing and the number of rolling operations. These results are shown in Table 5 below. Regarding the examples, tandem rolling was performed, and in the comparative examples, single rolling was performed. ◎ indicates good, ○ indicates slightly good, Δ indicates slightly poor, and x indicates poor.
[0056]
[Table 5]
[Table 6]
As shown in Tables 5 and 6 above, in Examples 20 to 22, the aluminum alloy ingot having an appropriate composition was subjected to appropriate cold rolling to obtain an aluminum alloy plate, so that good mechanical properties and tearing were achieved. Sex was obtained. Furthermore, high productivity and low production cost were possible.
[0059]
On the other hand, in Comparative Example 23, the plate thickness is too thin to be evaluated, but due to the high strength, it is predicted that the drop impact resistance and the rivet overhang limit height are inferior. In Comparative Examples 28 to 30, since the cold rolling rate is less than the lower limit of the range of the present invention, the strength required for the negative pressure canister stub tab end material cannot be obtained, and the can opening load is high.
[0060]
In Comparative Examples 24 and 26, since the end temperature of the cold rolling process is less than the lower limit of the range of the present invention, the rivet stretchability is slightly inferior, but other characteristics are good. However, since high-speed cold rolling becomes difficult, the productivity is about half that of the present invention, and the manufacturing cost is about 1.3 times that of the present invention. In Comparative Examples 25 and 27, since the end temperature of the cold rolling process exceeds the upper limit of the range of the present invention, in addition to the productivity and the manufacturing cost, the can open load at the time of pop is high, and the negative pressure can steion The tab type end material is insufficient.
[0061]
【The invention's effect】
As described above in detail, according to the present invention, an aluminum alloy ingot having an appropriate composition is used, and an Al—Fe—Mn-based crystallized product and Mg—Si are obtained by a cold rolling process after the hot rolling process. Since the system crystallized product is generated appropriately, the can opening load can be reduced while maintaining sufficient strength. As a result, the negative pressure can Steion tab type end material used for cans of beverages that do not contain carbonated beverages such as fruit juice beverages and coffee, etc., the load at the time of opening after heat treatment such as retort treatment and repair treatment is low, the end In addition to being able to satisfy the characteristics sufficiently, it is possible to achieve high productivity and low manufacturing cost, and it is possible to sufficiently adapt to the increase in thickness and strength. Moreover, productivity can be improved more by using a tandem rolling mill at the time of a cold rolling process.
[Brief description of the drawings]
FIG. 1 is a schematic diagram showing a test method for can openability.
FIG. 2 is a schematic diagram showing a drop impact resistance test method.
[Explanation of symbols]
1, 11;
Claims (6)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
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| JP07867299A JP3853103B2 (en) | 1999-03-23 | 1999-03-23 | Method for producing aluminum alloy sheet with excellent openability |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP07867299A JP3853103B2 (en) | 1999-03-23 | 1999-03-23 | Method for producing aluminum alloy sheet with excellent openability |
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| JP3853103B2 true JP3853103B2 (en) | 2006-12-06 |
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| JP5388084B2 (en) * | 2007-07-27 | 2014-01-15 | 三菱アルミニウム株式会社 | Aluminum alloy clad material for heat exchangers with excellent strength and pitting corrosion resistance |
| JP5961839B2 (en) * | 2009-03-31 | 2016-08-02 | 株式会社神戸製鋼所 | Aluminum alloy plate for can body and manufacturing method thereof |
| EP2703508B1 (en) * | 2012-08-28 | 2016-03-30 | Hydro Aluminium Rolled Products GmbH | Aluminium alloy resistant to intercrystalline corrosion |
| JP5954099B2 (en) * | 2012-10-12 | 2016-07-20 | 日本軽金属株式会社 | Aluminum alloy sheet for battery cases with excellent formability, heat dissipation and weldability |
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