JP2015059251A - Aluminum alloy sheet for negative-pressure can lid - Google Patents
Aluminum alloy sheet for negative-pressure can lid Download PDFInfo
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- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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Abstract
Description
本発明は、負圧缶蓋用アルミニウム合金板に係り、缶蓋としての必要強度を確保した上で、特にリベット成形性に優れ、薄肉化に適した負圧缶蓋用アルミニウム合金板に関するものである。 The present invention relates to an aluminum alloy plate for a negative pressure can lid, and particularly to an aluminum alloy plate for a negative pressure can lid that is excellent in rivet formability and suitable for thinning, while ensuring the necessary strength as a can lid. is there.
従来、特に飲料用の包装容器として、有底円筒状の胴部と蓋部からなる２ピースタイプのアルミニウム缶が広く使用されている。
＜缶蓋の一般的な製造工程について＞
このようなアルミニウム缶を構成する缶蓋は、次のような工程で製造される。まず、素材となる缶蓋用アルミニウム合金板に、耐食性を確保するためのクロメート処理等の化成処理を施した後、前記化成処理を施した缶蓋用アルミニウム合金板の片面、あるいは両面に塗装及び焼き付けを行う。
2. Description of the Related Art Conventionally, as a packaging container for beverages, a two-piece type aluminum can having a cylindrical body with a bottom and a lid has been widely used.
<General manufacturing process for can lids>
A can lid constituting such an aluminum can is manufactured by the following process. First, after applying chemical conversion treatment such as chromate treatment to ensure corrosion resistance to the aluminum alloy plate for can lid as a raw material, coating and coating on one side or both sides of the aluminum alloy plate for can lid subjected to the chemical conversion treatment Bake.
次に、塗装、焼付された前記缶蓋用アルミニウム合金板を所定の形状にブランキングした後、シェル成形を行う。続いて、前記シェル成形された缶蓋用アルミニウム合金板に、缶胴と巻締めするための巻締め部（カール部）を成形して缶蓋とし、この缶蓋の巻締め部にラバーを注入するコンパウンドライニングを行う。その後、バブル成形及びボタン成形を施すリベット成形工程、開口部の溝加工を施すスコア加工、凹凸及び文字等の加工を施すビード・エンボス成形工程、及びタブ付けを施すステイク成形工程を含めたコンバージョン成形を行う。最後に、缶胴に内容物を充填した後、前記缶胴と前記成形加工が施された缶蓋の巻締めを行い、洗浄及び殺菌を行う。 Next, the painted and baked aluminum alloy plate for can lids is blanked into a predetermined shape, and then shell molding is performed. Subsequently, a winding part (curl part) for fastening the can body and the can body is formed on the shell-formed aluminum alloy plate for the can lid to form a can lid, and rubber is injected into the winding part of the can lid. Perform compound drying. After that, conversion molding including rivet molding process for bubble molding and button molding, score processing for groove processing of openings, bead / emboss molding process for processing irregularities and letters, and stake molding process for tabbing I do. Finally, after filling the contents of the can body, the can body and the can lid subjected to the molding process are wound and cleaned and sterilized.
＜缶蓋の要求特性について＞
缶蓋は、缶胴と巻き締めされる際、カール部の寸法にバラツキがあると巻き締め不良が発生することがあり、缶蓋には厳しい寸法精度が求められる。さらに、巻き締め後、殺菌工程の加熱によって内圧が上昇しても反転（バックリング）しないだけの耐圧強度や、消費者の手に渡った後、タブを起こし（或は引っ張り）開缶する際、不具合なく飲み口が開口することが求められる。
＜材料の要求特性について＞
このような缶蓋を得るため、材料となるアルミニウム合金板には缶蓋への成形性、巻き締め不良抑制のための低い変形異方性、耐圧強度を得るための材料強度、開缶不良を起こさないためのリベット成形性や引き裂き性（開缶性）などが求められる。
<About required characteristics of can lid>
When the can lid and the can body are tightened, if the curled portion has a variation in dimensions, winding failure may occur, and the can lid is required to have strict dimensional accuracy. Furthermore, after winding, when the inner pressure rises due to heating during the sterilization process, the pressure strength is such that it does not reverse (buckling), and after reaching the consumer's hand, the tab is raised (or pulled) to open the can It is required that the mouth open without any trouble.
<Required properties of materials>
In order to obtain such a can lid, the aluminum alloy plate used as a material has a moldability to the can lid, a low deformation anisotropy for suppressing poor winding, a material strength for obtaining a pressure resistance, and a can open failure. Rivet formability and tearability (can openability) to prevent it from occurring are required.
一方、従来より、果汁、コーヒー、紅茶等の負圧缶の缶蓋用アルミニウム合金として、ＡＡ５０５２やＡＡ５０２１が用いられているが、前記要求特性に鑑み、従来合金より比較的高い濃度のＭｎを含有する負圧缶蓋用アルミニウム合金板に関する技術が開発されてきた（特許文献１〜６）。
On the other hand, conventionally, AA5052 and AA5021 are used as aluminum alloys for cans of negative pressure cans such as fruit juice, coffee, tea, etc., but in view of the required characteristics, it contains Mn at a relatively higher concentration than conventional alloys. Techniques relating to aluminum alloy plates for negative pressure can lids have been developed (
ところで、特許文献１〜６の実施例では、０．２３〜０．２５ｍｍの板厚を有する負圧缶蓋用アルミニウム合金板が製造されている。一方、近年、コストダウンや省資源の観点から飲料容器の更なる薄肉化（板厚：０．２２０ｍｍ未満）が要求されており、負圧缶蓋用アルミニウム合金板も薄肉化に対応していく必要がある。負圧缶蓋用アルミニウム合金板を薄肉化すると、耐圧強度やリベット成形性が低下するが、耐圧強度については、缶蓋形状の工夫によってある程度確保できる。従って、負圧缶蓋用アルミニウム合金板としては、特にリベット成形性の確保が要求される。 By the way, in the Example of patent documents 1-6, the aluminum alloy plate for negative pressure can lids which has plate thickness of 0.23-0.25 mm is manufactured. On the other hand, in recent years, there has been a demand for further thinning of beverage containers (thickness: less than 0.220 mm) from the viewpoint of cost reduction and resource saving, and aluminum alloy plates for negative pressure can lids will also respond to thinning. There is a need. When the aluminum alloy plate for a negative pressure can lid is made thinner, the pressure strength and rivet formability are lowered, but the pressure strength can be secured to some extent by devising the shape of the can lid. Accordingly, as the aluminum alloy plate for the negative pressure can lid, it is particularly required to ensure rivet formability.
特許文献１〜６に記載された缶蓋用アルミニウム合金板は、従来合金（ＡＡ５０５２，ＡＡ５０２１）より高Ｍｎ化したことによってＡｌ−Ｆｅ−Ｍｎ系金属間化合物が増大し、これが前記アルミニウム合金板の引き裂き性の向上や変形異方性（耳率）の低減に寄与している。しかし、その反面、増大したＡｌ−Ｆｅ−Ｍｎ系金属間化合物は亀裂の起点や伝播経路となって、前記アルミニウム合金板のリベット成形性に悪影響を及ぼす。このため、特許文献１〜６に記載された缶蓋用アルミニウム合金板は、更なる薄肉化に十分対応し得るものとはいえない。
The aluminum alloy plate for can lids described in
本発明は、従来技術の上記問題点に鑑みてなされたもので、従来合金より比較的高い濃度のＭｎを含有する負圧缶蓋用アルミニウム合金板において、これをさらに薄肉化した場合でも、優れたリベット成形性を備える負圧缶蓋用アルミニウム合金板を提供することを目的とする。 The present invention has been made in view of the above-mentioned problems of the prior art, and in an aluminum alloy plate for negative pressure can lids containing Mn at a relatively higher concentration than conventional alloys, it is excellent even when this is further thinned. Another object of the present invention is to provide an aluminum alloy plate for a negative pressure can lid having rivet formability.
前記課題を解決するため、本発明者らは比較的高い濃度のＭｎを含有するアルミニウム合金板のリベット成形性について種々検討したところ、アルミニウム合金中の各元素を所定の範囲とした上で、Ｆｅ、Ｍｎ、Ｍｇ量を所定の関係式の範囲内に管理することで、リベット成形性が向上することを見出した。
本発明に係る負圧缶蓋用アルミニウム合金板は、Ｓｉを０．１０質量％以上、０．４０質量％以下、Ｆｅを０．２０質量％以上、０．４０質量％以下、Ｃｕを０．１０質量％以上、０．３０質量％以下、Ｍｎを０．３０質量％以上、１．００質量％以下、Ｍｇを１．００質量％以上、２．００質量％以下の範囲で含有し、残部がＡｌ及び不可避不純物からなり、Ｆｅの質量％を［Ｆｅ］、Ｍｎの質量％を［Ｍｎ］、Ｍｇの質量％を［Ｍｇ］としたとき、下記不等式（１）を満たす。
１．０５≦［Ｆｅ］＋１．０７［Ｍｎ］＋０．２７［Ｍｇ］≦１．６５・・・（１）
本発明に係るアルミニウム合金板は、望ましくは、さらにＺｎを０．０５質量％以上、０．２５質量％以下の範囲で含有することができる。
In order to solve the above-mentioned problems, the present inventors have made various studies on the rivet formability of an aluminum alloy plate containing a relatively high concentration of Mn. After making each element in the aluminum alloy into a predetermined range, Fe It has been found that rivet formability is improved by managing the amounts of Mn and Mg within the range of the predetermined relational expression.
In the aluminum alloy plate for a negative pressure can lid according to the present invention, Si is 0.10 mass% or more and 0.40 mass% or less, Fe is 0.20 mass% or more and 0.40 mass% or less, and Cu is 0.0. 10% by mass or more, 0.30% by mass or less, Mn 0.30% by mass or more and 1.00% by mass or less, Mg in a range of 1.00% by mass or more and 2.00% by mass or less, and the balance Is composed of Al and inevitable impurities, and when the mass% of Fe is [Fe], the mass% of Mn is [Mn], and the mass% of Mg is [Mg], the following inequality (1) is satisfied.
1.05 ≦ [Fe] +1.07 [Mn] +0.27 [Mg] ≦ 1.65 (1)
The aluminum alloy plate according to the present invention can desirably further contain Zn in a range of 0.05% by mass to 0.25% by mass.
本発明に係るアルミニウム合金板は、従来の負圧缶蓋用アルミニウム合金板より薄肉化（例えば０．２２０ｍｍ未満）した場合にも、優れたリベット成形性を示す。また、本発明に係るアルミニウム合金板は、耐圧強度を得るための材料強度、缶蓋への成形性、巻き締め不良抑制のための低い変形異方性、引き裂き性などにも優れ、主としてＳＯＴ（ステイオンタブ）式の負圧缶蓋として好適に用いることができる。 The aluminum alloy plate according to the present invention exhibits excellent rivet formability even when it is made thinner (for example, less than 0.220 mm) than a conventional aluminum alloy plate for a negative pressure can lid. In addition, the aluminum alloy plate according to the present invention is excellent in material strength for obtaining pressure resistance strength, formability to a can lid, low deformation anisotropy for suppressing poor winding, tearability, and the like. Steion tab) type negative pressure can lid can be suitably used.
始めに、本発明に係る負圧缶蓋用アルミニウム合金板の成分組成について説明する。
＜Ｓｉ：０．１０質量％以上、０．４０質量％以下＞
Ｓｉは、アルミニウム合金中にＭｇ−Ｓｉ系、Ａｌ−Ｆｅ−Ｍｎ−Ｓｉ系晶出物を形成し、熱間圧延後の再結晶を促進させる効果がある。Ｓｉの含有量が０．１０質量％未満の場合、アルミニウム合金板の原材料に使用できるスクラップ量が減少するとともに、アルミニウム地金の必要純度が高くなるため、コストが増大する。一方、Ｓｉの含有量が０．４０質量％を超える場合、熱間圧延までの工程でアルミニウム合金中に微細なＡｌ−Ｆｅ−Ｍｎ−Ｓｉ系析出物が多数生じて熱間圧延後の再結晶を阻害し、リベット成形性を低下させる。従って、Ｓｉの含有量は０．１０質量％以上、０．４０質量％以下とする。
First, the component composition of the aluminum alloy plate for negative pressure can lids according to the present invention will be described.
<Si: 0.10% by mass or more and 0.40% by mass or less>
Si has the effect of forming Mg-Si-based and Al-Fe-Mn-Si-based crystals in the aluminum alloy and promoting recrystallization after hot rolling. When the Si content is less than 0.10% by mass, the amount of scrap that can be used as the raw material for the aluminum alloy sheet is reduced, and the required purity of the aluminum ingot is increased, which increases the cost. On the other hand, when the Si content exceeds 0.40 mass%, many fine Al—Fe—Mn—Si based precipitates are generated in the aluminum alloy in the process up to hot rolling, and recrystallization after hot rolling. Hinders the rivet formability. Accordingly, the Si content is set to 0.10% by mass or more and 0.40% by mass or less.
＜Ｆｅ：０．２０質量％以上、０．４０質量％以下＞
Ｆｅは、アルミニウム合金中にＡｌ−Ｆｅ−Ｍｎ系、Ａｌ−Ｆｅ−Ｍｎ−Ｓｉ系晶出物を形成し、熱間圧延後の再結晶を促進させる効果がある。Ｆｅの含有量が０．２０質量％未満の場合、前記晶出物が不足して熱間圧延後の再結晶が不十分となり、リベット成形性が低下する。一方、Ｆｅの含有量が０．４０質量％を超える場合、アルミニウム合金板中の晶出物が大きく、また過剰に形成され、リベット成形性が低下する。従って、Ｆｅの含有量は０．２０質量％以上、０．４０質量％以下とする。
<Fe: 0.20 mass% or more and 0.40 mass% or less>
Fe has the effect of forming Al—Fe—Mn and Al—Fe—Mn—Si crystals in an aluminum alloy and promoting recrystallization after hot rolling. When the Fe content is less than 0.20% by mass, the crystallized matter is insufficient, recrystallization after hot rolling becomes insufficient, and rivet formability is deteriorated. On the other hand, when the Fe content exceeds 0.40% by mass, the crystallized material in the aluminum alloy plate is large and excessively formed, and the rivet formability is lowered. Therefore, the Fe content is set to 0.20 mass% or more and 0.40 mass% or less.
＜Ｃｕ：０．１０質量％以上、０．３０質量％以下＞
Ｃｕは、アルミニウム合金板の強度を向上させる効果がある。Ｃｕの含有量が０．１０質量％未満の場合、アルミニウム合金板の強度が不十分であり、缶蓋に成形されたときの耐圧強度が不足する。一方、Ｃｕの含有量が０．３０質量％を超える場合、アルミニウム合金板の強度が過剰となり、リベット成形性が低下する。従って、Ｃｕの含有量は０．１０質量％以上、０．３０質量％以下とする。
<Cu: 0.10% by mass or more and 0.30% by mass or less>
Cu has the effect of improving the strength of the aluminum alloy plate. When the content of Cu is less than 0.10% by mass, the strength of the aluminum alloy plate is insufficient, and the pressure strength when formed into a can lid is insufficient. On the other hand, when the Cu content exceeds 0.30% by mass, the strength of the aluminum alloy plate becomes excessive, and the rivet formability decreases. Therefore, the Cu content is set to 0.10 mass% or more and 0.30 mass% or less.
＜Ｍｎ：０．３０質量％以上、１．００質量％以下＞
Ｍｎは、アルミニウム合金板の強度を向上させる効果があるとともに、アルミニウム合金板中にＡｌ−Ｆｅ−Ｍｎ系、Ａｌ−Ｆｅ−Ｍｎ−Ｓｉ系晶出物を形成させ、熱間圧延後の再結晶を促進させる効果がある。Ｍｎの含有量が０．３０質量％未満の場合、アルミニウム合金板の強度が不十分となるとともに、熱間圧延後の再結晶が不十分となってリベット成形性が低下する。一方、Ｍｎの含有量が１．００質量％以上の場合、アルミニウム合金板中の晶出物が大きく、また過剰に形成され、リベット成形性を低下させる。従って、Ｍｎの含有量は０．３０質量％以上、１．００質量％以下とする。望ましい範囲は０．５０質量％以上、０．８０質量％未満である。
<Mn: 0.30 mass% or more and 1.00 mass% or less>
Mn has the effect of improving the strength of the aluminum alloy sheet, and forms Al-Fe-Mn and Al-Fe-Mn-Si crystals in the aluminum alloy sheet, and recrystallizes after hot rolling. Has the effect of promoting When the content of Mn is less than 0.30% by mass, the strength of the aluminum alloy sheet becomes insufficient, and recrystallization after hot rolling becomes insufficient, thereby reducing the rivet formability. On the other hand, when the Mn content is 1.00% by mass or more, the crystallized material in the aluminum alloy sheet is large and excessively formed, and the rivet formability is lowered. Accordingly, the Mn content is set to 0.30 mass% or more and 1.00 mass% or less. A desirable range is 0.50 mass% or more and less than 0.80 mass%.
＜Ｍｇ：１．００質量％以上、２．００質量％以下＞
Ｍｇは、アルミニウム合金板の強度を向上させる効果がある。Ｍｇの含有量が１．００質量％未満の場合、アルミニウム合金板の強度が不十分であり、缶蓋に成形されたときの耐圧強度が不足する。一方、Ｍｇの含有量が２．００質量％を超える場合、アルミニウム合金板の強度が過剰となり、リベット成形性が低下する。従って、Ｍｇの含有量は１．００質量％以上、２．００質量％以下とする。望ましい範囲は１．００質量％以上、１．８０質量％未満、さらに望ましい範囲は、１．２質量％以上、１．５０質量％未満である。
<Mg: 1.00 mass% or more and 2.00 mass% or less>
Mg has the effect of improving the strength of the aluminum alloy plate. When the Mg content is less than 1.00% by mass, the strength of the aluminum alloy plate is insufficient, and the pressure strength when formed into a can lid is insufficient. On the other hand, when the Mg content exceeds 2.00% by mass, the strength of the aluminum alloy plate becomes excessive, and the rivet formability decreases. Therefore, the Mg content is set to 1.00% by mass or more and 2.00% by mass or less. A desirable range is 1.00% by mass or more and less than 1.80% by mass, and a further desirable range is 1.2% by mass or more and less than 1.50% by mass.
＜Ｚｎ：０．０５質量％以上、０．２５質量％以下＞
Ｚｎは、アルミニウム合金板の結晶粒を微細化させ、リベット成形性を向上させる効果があるため、必要に応じて添加される。Ｚｎの含有量が０．０５質量％未満の場合、前記効果が十分得られない。一方、Ｚｎの含有量が０．２５質量％を超える場合、熱間圧延後の冷却中などに、Ａｌ−Ｃｕ−Ｍｇ−Ｚｎ系析出物が粒界偏析し、リベット成形性がかえって低下する。従って、Ｚｎを添加する場合、含有量は０．０５質量％以上、０．２５質量％以下とする。望ましい範囲は０．０８質量％以上、さらに望ましい範囲は０．１２質量％以上である。
<Zn: 0.05 mass% or more and 0.25 mass% or less>
Zn has the effect of refining the crystal grains of the aluminum alloy plate and improving the rivet formability, so it is added as necessary. When the Zn content is less than 0.05% by mass, the above effect cannot be obtained sufficiently. On the other hand, when the Zn content exceeds 0.25 mass%, during cooling after hot rolling, Al-Cu-Mg-Zn-based precipitates segregate at the grain boundaries, and the rivet formability decreases. Therefore, when Zn is added, the content is set to 0.05% by mass or more and 0.25% by mass or less. A desirable range is 0.08% by mass or more, and a more desirable range is 0.12% by mass or more.
＜不可避不純物＞
本発明に係るアルミニウム合金板は、ほかに不可避不純物を含有する。不可避不純物として、Ｃｒ、Ｔｉ、Ｚｒはそれぞれ０．１５質量％以下、好ましくはそれぞれ０．０５質量％以下、その他の元素としてＶ、Ｎｉ、Ｉｎ、Ｓｎ、Ｇａなどはそれぞれ０．０５質量％以下の範囲で含有が許容される。
<Inevitable impurities>
The aluminum alloy plate according to the present invention additionally contains inevitable impurities. As unavoidable impurities, Cr, Ti, Zr are each 0.15% by mass or less, preferably 0.05% by mass or less, and as other elements, V, Ni, In, Sn, Ga, etc. are each 0.05% by mass or less. Inclusion in the range of is acceptable.
＜前記不等式（１）＞
Ｆｅ、Ｍｎは、アルミニウム合金中にＡｌ−Ｆｅ−Ｍｎ系、Ａｌ−Ｆｅ−Ｍｎ−Ｓｉ系の晶出物を形成する。熱間圧延中、この晶出物の近傍に不均一変形領域が形成されて歪みが集中し、その領域が再結晶核となり、熱間圧延後の再結晶を促進させる。また、Ｍｇは、熱間圧延中の蓄積歪みを増大させ、熱間圧延後の再結晶を促進させる作用を有する。Ｆｅ、Ｍｎによる晶出物の量と、Ｍｇによる蓄積歪みの量は、熱間圧延後の再結晶を促進するとの観点からは相互補完的である。熱間圧延後に適正な再結晶組織が得られれば、冷間圧延後の冷間圧延板（製品板）のリベット成形性が向上する。
<Inequality (1)>
Fe and Mn form Al-Fe-Mn-based and Al-Fe-Mn-Si-based crystals in the aluminum alloy. During hot rolling, a non-uniform deformation region is formed in the vicinity of the crystallized product, and strain is concentrated. This region becomes a recrystallization nucleus and promotes recrystallization after hot rolling. Moreover, Mg has the effect | action which increases the accumulation distortion in hot rolling and accelerates recrystallization after hot rolling. The amount of crystallized material due to Fe and Mn and the amount of accumulated strain due to Mg are mutually complementary from the viewpoint of promoting recrystallization after hot rolling. If an appropriate recrystallized structure is obtained after hot rolling, the rivet formability of the cold rolled sheet (product sheet) after cold rolling is improved.
一方、Ｆｅ、Ｍｎの含有量が過剰になると粗大な晶出物が形成され、また、Ｍｇは鋳造の際にアルミニウム合金の固相線温度を低下させ、晶出物を成長させる。粗大な晶出物が形成されると、該晶出物が割れの起点及び伝播経路となり、リベット成形性が低下する。
従って、粗大な晶出物の形成を抑制し、かつ熱間圧延後に適正な再結晶組織を得て、冷間圧延後の冷間圧延板（製品板）のリベット成形性を向上させるには、Ｆｅ、Ｍｎ、Ｍｇの含有量を適切な関係で管理する必要がある。
Ａｌ−Ｍｇ−Ｍｎ系アルミニウム合金において、粗大晶出物の形成は、［Ｆｅ］、［Ｍｎ］、［Ｍｇ］をパラメーターとして、［Ｆｅ］＋１．０７［Ｍｎ］＋０．２７［Ｍｇ］の大きさに依存し、この値が１．６５を超える場合、粗大な晶出物が生じる。一方、［Ｆｅ］＋１．０７［Ｍｎ］＋０．２７［Ｍｇ］の値が１．０５未満の場合、Ｆｅ、Ｍｎ及びＭｇの作用が不足し、熱間圧延後に適正な再結晶組織を得ることができない。すなわち、［Ｆｅ］＋１．０７［Ｍｎ］＋０．２７［Ｍｇ］が１．０５〜１．６５の範囲内において、粗大な晶出物の形成を抑制し、かつ熱間圧延後に適正な再結晶組織を得て、冷間圧延後の冷間圧延板（製品板）のリベット成形性を向上させることができる。
On the other hand, if the contents of Fe and Mn are excessive, coarse crystallized substances are formed, and Mg lowers the solidus temperature of the aluminum alloy during casting to grow the crystallized substances. When a coarse crystallized product is formed, the crystallized product becomes a starting point and a propagation path of cracking, and the rivet formability decreases.
Therefore, in order to suppress the formation of coarse crystallized material, obtain an appropriate recrystallized structure after hot rolling, and improve the rivet formability of the cold rolled plate (product plate) after cold rolling, It is necessary to manage the contents of Fe, Mn, and Mg in an appropriate relationship.
In an Al—Mg—Mn-based aluminum alloy, the formation of coarse crystals is as large as [Fe] +1.07 [Mn] +0.27 [Mg] with [Fe], [Mn], and [Mg] as parameters. Depending on the thickness, if this value exceeds 1.65, coarse crystallisation occurs. On the other hand, when the value of [Fe] +1.07 [Mn] +0.27 [Mg] is less than 1.05, the action of Fe, Mn and Mg is insufficient, and an appropriate recrystallized structure is obtained after hot rolling. I can't. That is, when [Fe] + 1.07 [Mn] + 0.27 [Mg] is within the range of 1.05 to 1.65, the formation of coarse crystals is suppressed, and proper recrystallization is performed after hot rolling. A structure can be obtained and the rivet formability of the cold rolled sheet (product sheet) after cold rolling can be improved.
本発明に係るアルミニウム合金板は、鋳造、均質化熱処理、熱間圧延、及び冷間圧延の工程で製造することができる。
鋳造は、半連続鋳造法（ＤＣ鋳造）が用いられる。
均質化熱処理は、ＤＣ鋳造で得られた鋳塊を４８０〜６２０℃に２〜１０時間保持する条件で、１回又は２回行う。処理温度が４８０℃未満では溶質元素の均質化が不十分となり、処理温度が６２０℃を超えると鋳塊の表面で局部的な溶融（バーニング）が生じるおそれがある。保持時間は２時間以上であれば均質化が可能で、１０時間を超えるとエネルギーコストが無駄になる。この均質化熱処理は、後続の熱間圧延の予備加熱を兼ねる。
The aluminum alloy plate according to the present invention can be produced by the steps of casting, homogenizing heat treatment, hot rolling, and cold rolling.
For casting, a semi-continuous casting method (DC casting) is used.
Homogenization heat processing is performed once or twice on the conditions which hold | maintain the ingot obtained by DC casting at 480-620 degreeC for 2 to 10 hours. If the treatment temperature is less than 480 ° C., the solute elements are not sufficiently homogenized. If the treatment temperature exceeds 620 ° C., local melting (burning) may occur on the surface of the ingot. If the holding time is 2 hours or more, homogenization is possible, and if it exceeds 10 hours, energy costs are wasted. This homogenization heat treatment also serves as preheating for subsequent hot rolling.
熱間圧延は、粗圧延（リバース圧延）と仕上げ圧延（タンデム圧延）の組合せで行うことが望ましい。熱間圧延の終了温度（巻き取り温度）は３００〜３７０℃とする。この温度で巻き取ることにより、熱間圧延板は再結晶組織となる。冷間圧延後のアルミニウム合金板において優れたリベット成形性を得るには、熱間圧延板の再結晶率は９０％以上（未再結晶部が１０％未満）が必要である。巻き取り温度が３００℃以下の場合、熱間圧延板の再結晶率が低下し、冷間圧延後の冷間圧延板（製品板）のリベット成形性が低下する。
冷間圧延は、８０〜９３％の圧延率で行い、冷間圧延の前又は途中で中間焼鈍を行わない。冷間圧延の圧延率が８０％未満では缶蓋としての強度が不足し、９３％を超えると耐力が上がりすぎて成形性が低下し、また変形異方性（耳率）が大きくなる。
なお、以上説明した製造工程及び条件は、従来の負圧缶蓋用アルミニウム合金板の製造工程及び条件と特に変わるものではない。
Hot rolling is preferably performed by a combination of rough rolling (reverse rolling) and finish rolling (tandem rolling). The end temperature (winding temperature) of hot rolling is 300 to 370 ° C. By winding at this temperature, the hot-rolled sheet becomes a recrystallized structure. In order to obtain excellent rivet formability in an aluminum alloy sheet after cold rolling, the recrystallization rate of the hot rolled sheet needs to be 90% or more (the unrecrystallized portion is less than 10%). When the coiling temperature is 300 ° C. or less, the recrystallization rate of the hot rolled sheet is lowered, and the rivet formability of the cold rolled sheet (product sheet) after cold rolling is lowered.
Cold rolling is performed at a rolling rate of 80 to 93%, and intermediate annealing is not performed before or during the cold rolling. When the rolling rate of cold rolling is less than 80%, the strength as a can lid is insufficient, and when it exceeds 93%, the yield strength is excessively increased, the formability is lowered, and the deformation anisotropy (ear ratio) is increased.
The manufacturing process and conditions described above are not particularly different from the manufacturing process and conditions of a conventional aluminum alloy plate for negative pressure can lid.
表１に示すアルミニウム合金を、半連続鋳造法（ＤＣ）にて厚さ６００ｍｍの鋳塊とし、鋳塊表層を１５ｍｍ面削してスラブを作製した。このスラブに均質化熱処理、熱間圧延、及び冷間圧延を施し、板厚０．２１０ｍｍの負圧缶蓋用アルミニウム合金板に仕上げた。均質化処理の条件、熱間圧延の巻き取り温度、及び冷間圧延の圧延率を表１に示す。
熱間圧延後のアルミニウム合金板（熱間圧延材）を供試材として、以下の要領で再結晶率を求めた。また、冷間圧延後のアルミニウム合金板（冷間圧延板）を供試材として、以下の要領で０．２％耐力とリベット成形性を測定した。
The aluminum alloy shown in Table 1 was made into an ingot having a thickness of 600 mm by a semi-continuous casting method (DC), and the surface layer of the ingot was chamfered by 15 mm to produce a slab. The slab was subjected to homogenization heat treatment, hot rolling, and cold rolling to finish an aluminum alloy plate for a negative pressure can lid having a plate thickness of 0.210 mm. Table 1 shows the conditions for the homogenization treatment, the coiling temperature for hot rolling, and the rolling rate for cold rolling.
Using the aluminum alloy sheet (hot rolled material) after hot rolling as a test material, the recrystallization rate was determined in the following manner. Moreover, 0.2% yield strength and rivet formability were measured in the following manner using an aluminum alloy plate (cold rolled plate) after cold rolling as a test material.
＜再結晶率の測定＞
各供試材から試験片を切り出し、圧延方向及び板厚方向に平行となる断面が観察できるように研磨用樹脂に埋め込み、同断面を研磨して鏡面とし、次いでエッチングした後、倍率が１００倍の光学顕微鏡により結晶組織を観察し、再結晶率を測定した。供試材の板厚をｔ、板厚方向に測定した再結晶組織の厚みをｔｒ、同じく未再結晶部の厚みをｔｎとしたとき、ｔ＝ｔｒ＋ｔｎであり、再結晶率は（ｔｒ／ｔ）×１００で算出した。なお、再結晶組織は等軸粒からなり、未再結晶部は圧延方向に伸びた加工組織である。再結晶率の適正範囲は９０％以上とした。再結晶率が９０％以上であれば、冷間圧延後の冷間圧延板（アルミニウム合金板）のリベット成形性に問題が生じない。表１において、再結晶率の欄の○印は再結晶率が９０％以上、×印は９０％未満を意味する。
＜０．２％耐力＞
各供試材について、塗装・焼付け工程を模擬したオイルバスによる２５０℃×２０秒の熱処理を施した後、引張方向が圧延方向と平行になるＪＩＳ−５号引張試験片を作製し、ＪＩＳＺ２２４１の規定に準じて引張試験を行い、０．２％耐力を求めた。０．２％耐力の適性範囲は２４０ＭＰａ以上とした。０．２％耐力が２４０ＭＰａ以上であれば、薄肉化された缶蓋であっても耐圧強度を満足する。
<Measurement of recrystallization rate>
A specimen is cut out from each specimen, embedded in a polishing resin so that a cross section parallel to the rolling direction and the plate thickness direction can be observed, the cross section is polished to a mirror surface, and then etched, and then the magnification is 100 times. The crystal structure was observed with an optical microscope and the recrystallization rate was measured. The thickness of the test specimen t, when the thickness of the recrystallized structure was measured in the thickness direction t r, also the thickness of the non-recrystallized portion has a t n, a t = t r + t n, recrystallization ratio Was calculated by (t r / t) × 100. The recrystallized structure is composed of equiaxed grains, and the non-recrystallized part is a processed structure extending in the rolling direction. The appropriate range for the recrystallization rate was 90% or more. If the recrystallization rate is 90% or more, there is no problem in the rivet formability of the cold rolled sheet (aluminum alloy sheet) after cold rolling. In Table 1, “O” in the column of recrystallization rate means that the recrystallization rate is 90% or more, and “x” means less than 90%.
<0.2% yield strength>
About each test material, after performing the heat processing of 250 degreeC * 20 second by the oil bath which simulated the painting and baking process, the tension direction becomes parallel with a rolling direction, and the JIS-5 tension test piece is produced, JISZ2241 A tensile test was performed in accordance with the regulations to obtain a 0.2% yield strength. The suitable range of 0.2% proof stress was 240 MPa or more. When the 0.2% proof stress is 240 MPa or more, even a thin can lid satisfies the pressure strength.
＜リベット成形性の測定＞
各供試材について、塗装・焼付け工程を模擬したオイルバスによる２５０℃×２０秒の熱処理を施した後、各供試材から５０ｍｍ×５０ｍｍの試験片を作製し、バブル工程を模擬した張出試験を実施し、限界張出し高さを求めた。張出試験は、図１に示すように、試験片１を上下のダイス２，３の間に挟み、一定のしわ押さえ力で固定し、ポンチ４を試験片１の中央部に対し垂直に押し込んで張出加工を行った。ダイス２，３は穴の内径が６．６０ｍｍ、肩部半径が０．４０ｍｍ、ポンチ４は外径が６．００ｍｍ、頭部の中央平坦部の直径が１ｍｍ、頭部の肩部半径が２．５０ｍｍである。
この張出試験により、試験片１に割れやくびれの発生なしに張出加工が行える張出高さの限界値（限界張出高さ）を測定した。限界張出高さの適正範囲は１．４５ｍｍ以上とした。限界張出高さが１．４５ｍｍ以上であれば、実成形時に十分な高さのボタンを成形することができ、リベット成形性に優れ、ステイク工程によってタブをしっかりと固定することができる。なお、タブの固定が不十分だと、開缶時にタブが取れて飲み口が開口しない不具合が発生する。
<Measurement of rivet formability>
For each sample material, heat treatment was performed at 250 ° C. for 20 seconds using an oil bath simulating the painting / baking process, and then a 50 mm × 50 mm test piece was prepared from each sample material to simulate the bubble process. A test was conducted to determine the limit overhang height. In the overhang test, as shown in FIG. 1, the
By this overhang test, the limit value (limit overhang height) of the overhang height at which the overhanging process can be performed without causing cracks and constriction on the
表１に示すように、各成分の含有量が本発明の規定範囲内で、かつＦｅ、Ｍｎ及びＭｇ含有量が前記不等式（１）を満たすＮｏ．１〜８は、熱間圧延材の再結晶率が９０％以上と高く、冷間圧延材の耐力が高くリベット成形性に優れる。
一方、いずれかの成分の含有量が本発明の規定範囲外か、又はＦｅ、Ｍｎ及びＭｇ含有量が前記不等式（１）を満たさないＮｏ．９〜２３は、耐力又はリベット成形性のいずれかがＮｏ．１〜８に比べて劣る。このうち、Ｎｏ．９はＳｉ含有量が過剰で、Ｎｏ．１０はＦｅ含有量が不足し、Ｎｏ．１３はＭｎ含有量が不足し、Ｎｏ．２３はＦｅ、Ｍｎ及びＭｇ含有量が前記不等式（１）を満たさない（不等式（１）の中辺の値が１．０５未満）ため、いずれも再結晶率が低く、リベット成形性が劣っていた。Ｎｏ．１１はＣｕ含有量が不足し、Ｎｏ．１５はＭｇ含有量が不足していたため、いずれも耐力が低かった。Ｎｏ．１２，１４，１６，１７，１９は、Ｃｕ、Ｍｎ、Ｍｇ、Ｚｎ、Ｆｅのいずれか１種以上が過剰なため、リベット成形性が劣っていた。Ｎｏ．１８，２０，２１，２２は、Ｆｅ、Ｍｎ及びＭｇ含有量が前記不等式（１）を満たさず（不等式（１）の中辺の値が１．６５を超える）、Ｎｏ．１８，２０はさらにＦｅ又はＭｎが過剰なため、リベット成形性が劣っていた。
なお、Ｎｏ．１８は特許文献１の実施例の合金Ｃ、Ｎｏ．１９は特許文献１の実施例の合金Ｇ、Ｎｏ．２０は特許文献３の実施例の合金Ｎｏ．２、Ｎｏ．２１は特許文献４の合金Ｎｏ．４に相当する。
As shown in Table 1, the content of each component is within the specified range of the present invention, and the content of Fe, Mn and Mg satisfies the inequality (1). Nos. 1 to 8 have a high recrystallization rate of 90% or more for the hot-rolled material, high proof stress for the cold-rolled material, and excellent rivet formability.
On the other hand, the content of any component is out of the specified range of the present invention, or the content of Fe, Mn and Mg does not satisfy the inequality (1). Nos. 9 to 23 are No. of either proof stress or rivet formability. It is inferior to 1-8. Of these, No. No. 9 has an excessive Si content. No. 10 lacks Fe content. No. 13 lacks the Mn content. In No. 23, the Fe, Mn and Mg contents do not satisfy the inequality (1) (the value of the middle side of the inequality (1) is less than 1.05). It was. No. No. 11 lacks Cu content. No. 15 had a low proof stress because the Mg content was insufficient. No. 12, 14, 16, 17, and 19 were inferior in rivet formability because one or more of Cu, Mn, Mg, Zn, and Fe was excessive. No. Nos. 18, 20, 21, and 22 have Fe, Mn, and Mg contents not satisfying the inequality (1) (the value of the middle side of the inequality (1) exceeds 1.65). 18 and 20 were inferior in rivet formability due to excessive Fe or Mn.
In addition, No. No. 18 is an alloy C, No. 1 in the example of
１ アルミニウム合金板
２，３ ダイス
４ パンチ
1
Claims (2)
１．０５≦［Ｆｅ］＋１．０７［Ｍｎ］＋０．２７［Ｍｇ］≦１．６５・・・（１） Si is 0.10% by mass or more and 0.40% by mass or less, Fe is 0.20% by mass or more and 0.40% by mass or less, Cu is 0.10% by mass or more and 0.30% by mass or less, and Mn is 0.30% by mass or more, 1.00% by mass or less, Mg is contained in the range of 1.00% by mass or more and 2.00% by mass or less, the balance is made of Al and inevitable impurities, and the mass% of Fe is [ Fe], an aluminum alloy plate for a negative pressure can lid that satisfies the following inequality (1) when the mass% of Mn is [Mn] and the mass% of Mg is [Mg].
1.05 ≦ [Fe] +1.07 [Mn] +0.27 [Mg] ≦ 1.65 (1)
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61152549A (en) * | 1984-12-19 | 1986-07-11 | 東洋製罐株式会社 | Can |
| JPS63227738A (en) * | 1987-03-16 | 1988-09-22 | Sumitomo Light Metal Ind Ltd | Corrosion resistant aluminum alloy composite plate and its production |
| JP2000355723A (en) * | 1999-06-16 | 2000-12-26 | Kobe Steel Ltd | Aluminum alloy sheet and its production |
| JP2001214248A (en) * | 2000-01-28 | 2001-08-07 | Sky Alum Co Ltd | Method for producing aluminum alloy hard sheet for can lid |
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| JP5204517B2 (en) * | 2008-03-19 | 2013-06-05 | 株式会社神戸製鋼所 | Aluminum alloy plate for battery case and manufacturing method thereof |
| KR101306515B1 (en) * | 2010-03-30 | 2013-09-09 | 가부시키가이샤 고베 세이코쇼 | Aluminum alloy plate for battery case, and battery case |
| JP2013163835A (en) * | 2012-02-09 | 2013-08-22 | Kobe Steel Ltd | Aluminum alloy sheet for di can body |
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2013
- 2013-09-20 JP JP2013194734A patent/JP5699192B2/en not_active Expired - Fee Related
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2014
- 2014-08-28 WO PCT/JP2014/072591 patent/WO2015041021A1/en active Application Filing
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61152549A (en) * | 1984-12-19 | 1986-07-11 | 東洋製罐株式会社 | Can |
| JPS63227738A (en) * | 1987-03-16 | 1988-09-22 | Sumitomo Light Metal Ind Ltd | Corrosion resistant aluminum alloy composite plate and its production |
| JP2000355723A (en) * | 1999-06-16 | 2000-12-26 | Kobe Steel Ltd | Aluminum alloy sheet and its production |
| JP2001214248A (en) * | 2000-01-28 | 2001-08-07 | Sky Alum Co Ltd | Method for producing aluminum alloy hard sheet for can lid |
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| WO2015041021A1 (en) | 2015-03-26 |
| CN105555979A (en) | 2016-05-04 |
| JP5699192B2 (en) | 2015-04-08 |
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