JPH04325659A - Manufacture of aluminum alloy hard sheet for forming excellent in tearing property - Google Patents
Manufacture of aluminum alloy hard sheet for forming excellent in tearing propertyInfo
- Publication number
- JPH04325659A JPH04325659A JP12290191A JP12290191A JPH04325659A JP H04325659 A JPH04325659 A JP H04325659A JP 12290191 A JP12290191 A JP 12290191A JP 12290191 A JP12290191 A JP 12290191A JP H04325659 A JPH04325659 A JP H04325659A
- Authority
- JP
- Japan
- Prior art keywords
- cold rolling
- plate
- alloy
- rolling
- rate
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Withdrawn
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 37
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 21
- 238000000034 method Methods 0.000 claims abstract description 54
- 238000000137 annealing Methods 0.000 claims abstract description 44
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 44
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 43
- 239000000956 alloy Substances 0.000 claims abstract description 43
- 238000001816 cooling Methods 0.000 claims abstract description 36
- 238000005097 cold rolling Methods 0.000 claims abstract description 35
- 238000010438 heat treatment Methods 0.000 claims abstract description 24
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 16
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 16
- 238000005096 rolling process Methods 0.000 claims abstract description 16
- 238000005266 casting Methods 0.000 claims abstract description 14
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 238000002791 soaking Methods 0.000 claims description 13
- 239000012535 impurity Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 43
- 238000009749 continuous casting Methods 0.000 abstract description 9
- 230000008569 process Effects 0.000 abstract description 7
- 229910052802 copper Inorganic materials 0.000 abstract description 5
- 229910052749 magnesium Inorganic materials 0.000 abstract description 4
- 230000001105 regulatory effect Effects 0.000 abstract 3
- 239000000203 mixture Substances 0.000 description 18
- 230000000694 effects Effects 0.000 description 14
- 239000006185 dispersion Substances 0.000 description 10
- 238000004064 recycling Methods 0.000 description 9
- 239000011248 coating agent Substances 0.000 description 6
- 238000000576 coating method Methods 0.000 description 6
- 238000001125 extrusion Methods 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 238000003483 aging Methods 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000035622 drinking Effects 0.000 description 3
- 230000009471 action Effects 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000010422 painting Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 229910016583 MnAl Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 235000013405 beer Nutrition 0.000 description 1
- 235000013361 beverage Nutrition 0.000 description 1
- 235000014171 carbonated beverage Nutrition 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000011257 shell material Substances 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Continuous Casting (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】この発明はアルミニウム缶の缶体
における蓋材等として使用される成形用アルミニウム合
金硬質板の製造方法、、特にステイオンタブ方式のアル
ミニウム缶用の蓋材に適した、引き裂き性に優れかつ高
強度と良好な成形性を有するアルミニウム合金硬質板の
製造方法に関するものである。[Industrial Field of Application] The present invention relates to a method for manufacturing a hard aluminum alloy plate for forming, which is used as a lid material for the can body of an aluminum can, and is particularly suitable for a lid material for a stay-on tab type aluminum can. The present invention relates to a method for manufacturing an aluminum alloy hard plate having excellent tearability, high strength, and good formability.
【０００２】0002
【従来の技術】一般にアルミニウム缶の蓋材としては、
５０５２合金、５０８２合金、５１８２合金などの５０
００番系の合金が用いられており、特にビールその他の
炭酸飲料用の缶の蓋材、すなわち内圧が加わる用途の缶
の蓋材としては焼付塗装後の耐力で３００Ｎ／ｍｍ２
以上の高強度が要求され、そのためこのような用途では
５１８２合金が主流を占めている。[Prior Art] Generally, the lid material for aluminum cans is
50 such as 5052 alloy, 5082 alloy, 5182 alloy, etc.
No. 00 series alloys are used, and are particularly suitable for can lids for beer and other carbonated beverages, i.e. for applications where internal pressure is applied, with a yield strength of 300 N/mm2 after baking coating.
The above-mentioned high strength is required, and therefore 5182 alloy is the mainstream for such applications.
【０００３】一方、最近ではアルミニウム缶の再利用（
リサイクル）を容易にするため、缶胴と缶蓋を同一成分
組成の合金で構成すること、すなわち所謂ユニアロイ化
することが考えられており、このユニアロイ化のために
蓋材、胴材ともに３００４合金をベースとした合金を用
いることが提案されているが、３００４合金をベースと
した従来の蓋材では、５１８２合金と同等のレベルを得
ることが困難であり、５１８２合金と同等の強度レベル
を得るためには高い冷間加工度を必要としてしまうため
、蓋材としての成形性の問題が生じ、そのため実用化に
は至っていない。On the other hand, recently, aluminum cans have been reused (
In order to facilitate recycling (recycling), it is being considered to construct the can body and can lid from an alloy with the same composition, that is, to make it a so-called unialloy. It has been proposed to use an alloy based on 3004 alloy, but with conventional lid materials based on 3004 alloy, it is difficult to obtain a strength level equivalent to that of 5182 alloy. Since this requires a high degree of cold working, there are problems with formability as a lid material, and as a result, it has not been put to practical use.
【０００４】0004
【発明が解決しようとする課題】従来一般の飲料缶の開
缶方式としては、缶蓋に取付けられたタブを引上げるこ
とによりタブと缶蓋の一部（飲み口部分）が缶から完全
に分離される所謂プルオンタブ方式が多かったが、最近
では環境問題の点から、図１、図２に示すように缶蓋上
面１に取付けられたタブ２および缶蓋の飲み口部分３が
開缶時に缶から完全には分離されない所謂スイテオンタ
ブ方式を採用する傾向が高まっている。また既に述べた
ようにアルミニウム材料のリサイクルのため、使用済み
の缶体を回収して再溶解し、再び缶体に使用する傾向が
強まっており、このようなリサイクルを容易とするため
の実用化可能な方策を開発することが望まれるようにな
っている。[Problems to be Solved by the Invention] Conventional methods for opening beverage cans include pulling up a tab attached to the can lid to completely remove the tab and a portion of the can lid (drinking spout) from the can. In many cases, the so-called pull-on tab system was used in which the can is separated, but recently, due to environmental concerns, the tab 2 attached to the top surface 1 of the can lid and the drinking spout 3 of the can lid are separated when the can is opened, as shown in Figures 1 and 2. There is an increasing tendency to adopt the so-called sui-eon-tab method, in which the can is not completely separated from the can. Furthermore, as already mentioned, in order to recycle aluminum materials, there is a growing tendency to collect used can bodies, remelt them, and use them again as can bodies. It has become desirable to develop possible strategies.
【０００５】ところでプルオンタブ方式の缶では、タブ
を引上げることにより人間の手指の力で直接スコアー（
切取り線となる刻み込み部分）から引きちぎることにな
るが、ステイオンタブ方式ではこれとは異なり、図２、
図３に示すように、手指の力で直接飲み口部分３をスコ
アー４から引きちぎるのではなく、タブ２の把手部２Ａ
を引上げることによりタブ２の取付部（リベット部）５
を支点として梃子の作用によりタブ２の先端部２Ｂを下
げ、これにより飲み口部分３を押し下げて、その飲み口
部分３を一部を残しスコアー４から引き裂くことになる
。By the way, with pull-on tab type cans, by pulling up the tab, the score (
This is different from the stay-on tab method, as shown in Figure 2.
As shown in FIG. 3, instead of tearing the spout part 3 off the score 4 directly with the force of the fingers, the handle part 2A of the tab 2
By pulling up the mounting part (rivet part) 5 of the tab 2
Using this as a fulcrum, the tip 2B of the tab 2 is lowered by the action of a lever, thereby pushing down the spout portion 3, and tearing the spout portion 3 from the score 4, leaving only a portion.
【０００６】このようにステイオンタブ方式では、手指
の力を梃子の作用により間接的に利用しているため、開
缶時において飲み口部分がスムーズにスコアーから引き
裂かれるように力の入れ方を微妙に加減することはでき
ず、そのため力の入れ方によっては飲み口部分３がスコ
アー４から均一に引き裂かれず、開缶の失敗が生じるこ
とがある。このような問題は、タブの形状や強度、ある
いはスコアーの刻み込み寸法や形状などによってもある
程度は改善することができるが、素材面からは、開缶時
の引き裂き力が少なくて済む材料、すなわち引き裂き性
の良好な材料を開発することが望まれる。[0006] In this way, in the stay-on tab method, the force of the fingers is used indirectly through the action of leverage, so the amount of force applied must be adjusted so that the spout part is smoothly torn away from the score when opening the can. It is not possible to adjust the amount delicately, and therefore, depending on how force is applied, the spout portion 3 may not be evenly torn off from the score 4, resulting in a failure in opening the can. These problems can be alleviated to some extent by changing the shape and strength of the tab, or the dimensions and shape of the score indentation, but from a material standpoint, materials that require less tearing force when opening the can, i.e. It is desirable to develop materials with good tearability.
【０００７】この発明は以上の事情を背景としてなされ
たもので、高強度を有するとともに引き裂き性が良好で
しかもアルミニウム缶の蓋材に用いた場合のリサイクル
も容易な、ステイオンタブ方式のアルミニウム缶の蓋材
に適した成形用アルミニウム合金硬質板の製造方法を提
供することを目的とするものである。The present invention was made against the background of the above-mentioned circumstances, and provides a stay-on tab type aluminum can that has high strength, good tearability, and is easy to recycle when used as a lid material for aluminum cans. The purpose of this invention is to provide a method for manufacturing a hard aluminum alloy plate for forming suitable for use as a lid material.
【０００８】[0008]
【課題を解決するための手段】本発明者等は、上述の課
題を解決するため、種々実験検討を重ねた結果、胴材に
使用されている３００４合金に比較的近い成分系でその
成分組成を適切に設定すると同時に、連続鋳造圧延（薄
板連続鋳造）を適用した製造プロセスにおける各条件を
適切に設定することによって最終板における金属間化合
物の分散状態を適切に調整し、これによって、高強度で
かつ引き裂き性が良好であって、しかも胴材に比較的近
い成分系であるところからリサイクルも容易な蓋材が得
られることを見出し、この発明をなすに至った。[Means for Solving the Problems] In order to solve the above-mentioned problems, the inventors of the present invention, as a result of various experimental studies, have developed a composition system that is relatively similar to the 3004 alloy used for the body material. At the same time, by appropriately setting each condition in the manufacturing process that applies continuous casting and rolling (continuous sheet casting), the state of dispersion of intermetallic compounds in the final sheet is appropriately adjusted, thereby achieving high strength. The present inventors have discovered that a lid material that is easy to recycle can be obtained because it has a composition system that is relatively close to that of the shell material, has good tearability, and has led to the creation of this invention.
【０００９】具体的には、請求項１に記載の発明の成形
用アルミニウム合金硬質板の製造方法は、Ｍｇ１．０〜
３．０ｗｔ％、Ｃｕ０．０５〜０．５ｗｔ％、Ｍｎ０．
５〜２．０ｗｔ％、Ｆｅ０．１〜１．０ｗｔ％、Ｓｉ０
．１〜０．５ｗｔ％を含有し、かつＦｅとＭｎの合計含
有量が１．０〜３．０ｗｔ％の範囲内にあり、残部がＡ
ｌおよび不可避的不純物よりなる合金を、５０℃／ｓｅ
ｃ 以上の冷却速度で厚さ１５ｍｍ以下の薄板に鋳造し
、その後所要の中間板厚まで１次冷間圧延を施した後、
１℃／ｓｅｃ以上の昇温速度で４５０〜６００℃の範囲
内の温度に加熱して直ちにもしくは１２０ｓｅｃ 以下
の短時間保持後、１℃／ｓｅｃ 以上の冷却速度で冷却
する中間焼鈍を施し、さらに３０％以上の圧延率で最終
冷間圧延を施し、これによって表面における１．０μｍ
以上の金属間化合物の数が０．２ｍｍ２ 当り３０００
個以上でその平均径が１．０〜２．５μｍの範囲内にあ
り、しかもかつ表面における金属間化合物の最大径が１
０μｍ以下である板を得ることを特徴とするものである
。Specifically, the method for manufacturing an aluminum alloy hard plate for forming according to the invention described in claim 1 includes Mg1.0 to
3.0wt%, Cu0.05-0.5wt%, Mn0.
5-2.0wt%, Fe0.1-1.0wt%, Si0
．． 1 to 0.5 wt%, and the total content of Fe and Mn is within the range of 1.0 to 3.0 wt%, and the balance is A.
An alloy consisting of l and unavoidable impurities was heated at 50°C/se
After casting into a thin plate with a thickness of 15 mm or less at a cooling rate of c or more, and then performing primary cold rolling to the required intermediate plate thickness,
Intermediate annealing is performed by heating to a temperature in the range of 450 to 600 °C at a temperature increase rate of 1 °C/sec or more, immediately or after holding for a short time of 120 seconds or less, and then cooling at a cooling rate of 1 °C/sec or more, and then Final cold rolling is performed at a rolling rate of 30% or more, thereby reducing the thickness of 1.0 μm on the surface.
The number of intermetallic compounds is 3000 per 0.2 mm2.
or more, and the average diameter is within the range of 1.0 to 2.5 μm, and the maximum diameter of the intermetallic compound on the surface is 1.0 to 2.5 μm.
This method is characterized by obtaining a plate having a thickness of 0 μm or less.
【００１０】また請求項２に記載の発明の成形用アルミ
ニウム合金硬質板の製造方法は、請求項１に記載の方法
において、前記鋳造と前記１次冷間圧延との間に、さら
に３００〜６３０℃の範囲内の温度に１時間以上保持す
る均熱処理を行なうことを特徴とするものである。[0010] Furthermore, in the method for manufacturing a hard aluminum alloy plate for forming according to the second aspect of the present invention, in the method according to the first aspect, a rolling process of 300 to 630 mm is further carried out between the casting and the first cold rolling. It is characterized by carrying out soaking treatment in which the temperature is maintained at a temperature within the range of °C for 1 hour or more.
【００１１】さらに請求項３に記載の発明の成形用アル
ミニウム合金硬質板の製造方法は、請求項１または請求
項２に記載の方法において、前記１次冷間圧延の中途で
、１℃／ｓｅｃ 以上の加熱速度で５００〜６００℃の
範囲内の温度に加熱して直ちにもしくは１２０ｓｅｃ
以下の短時間保持後１℃／ｓｅｃ 以上の冷却速度で冷
却する焼鈍を施すことを特徴とするものである。[0011] Furthermore, the method for manufacturing an aluminum alloy hard plate for forming according to the invention according to claim 3 is the method according to claim 1 or claim 2, in which the heating rate is 1° C./sec in the middle of the first cold rolling. Immediately or for 120 seconds after heating to a temperature within the range of 500 to 600℃ at the above heating rate.
It is characterized by performing annealing by cooling at a cooling rate of 1° C./sec or more after being held for a short time as follows.
【００１２】そしてまた請求項４に記載の発明の成形用
アルミニウム合金硬質板の製造方法は、請求項１〜請求
項３のいずれかに記載の方法において、前記最終冷間圧
延の後、さらに１０〜１００℃／ｈｒの昇温速度で１２
０〜２００℃の範囲内の温度に加熱して３０分以上保持
しさらに１０〜１００℃／ｈｒの冷却速度で冷却する最
終焼鈍を施すことを特徴とするものである。[0012] Furthermore, the method for manufacturing a hard aluminum alloy plate for forming according to the invention according to claim 4 is the method according to any one of claims 1 to 3, in which after the final cold rolling, further 10 12 at a heating rate of ~100°C/hr
It is characterized by performing final annealing by heating to a temperature in the range of 0 to 200°C, holding for 30 minutes or more, and then cooling at a cooling rate of 10 to 100°C/hr.
【００１３】[0013]
【作用】先ずこの発明における素材アルミニウム合金の
成分組成範囲の限定理由を説明する。[Operation] First, the reason for limiting the composition range of the raw material aluminum alloy in this invention will be explained.
【００１４】Ｍｇ：ＭｇはＣｕやＳｉとの共存によりＭ
ｇ２ Ｓｉ、Ａｌ２ ＣｕＭｇの析出による時効硬化に
寄与するとともに、Ｍｇそのものも固溶強化に寄与する
。Ｍｇ量が１．０ｗｔ％未満では蓋材として必要な強度
が得られない。一方Ｍｇ量が３．０ｗｔ％を越えれば、
強度向上は期待できるが、回収したアルミニウム２ピー
ス缶をリサイクルのために再溶解した後の鋳塊（再生塊
）中のＭｇ量が多くなり、その再生塊から３０００番系
の胴材を製造する場合にはＭｇ濃度を稀釈するために純
アルミニウム地金を必要とするようになってしまい、こ
の発明の目的の一つであるリサイクルの容易さを達成で
きなくなる。そこでＭｇ量は１．０〜３．０ｗｔ％の範
囲内とした。Mg: Mg coexists with Cu and Si.
In addition to contributing to age hardening due to the precipitation of g2 Si and Al2 CuMg, Mg itself also contributes to solid solution strengthening. If the Mg amount is less than 1.0 wt%, the strength required as a lid material cannot be obtained. On the other hand, if the Mg amount exceeds 3.0wt%,
Although an improvement in strength can be expected, the amount of Mg in the ingot (regenerated ingot) after the recovered two-piece aluminum can is remelted for recycling will increase, and 3000 series body material will be manufactured from the recycled ingot. In this case, a pure aluminum ingot is required to dilute the Mg concentration, making it impossible to achieve ease of recycling, which is one of the objectives of the present invention. Therefore, the Mg amount was set within the range of 1.0 to 3.0 wt%.
【００１５】Ｃｕ：ＣｕはＭｇと同様にそれ自体で固溶
強化に寄与するとともに、Ｍｇとの共存によるＡｌ２
ＣｕＭｇの析出による時効硬化に寄与し、特にこの発明
のように蓋材などの焼付塗装を施して使用する用途では
上述の効果が大きく、焼付塗装後に高強度を有する材料
を得ることができる。Ｃｕ量が０．０５ｗｔ％未満では
その効果が少なく、０．５ｗｔ％を越えれば時効硬化は
容易に得られる反面、硬くなり過ぎてその後の成形に不
利となるから、Ｃｕ量は０．０５〜０．５ｗｔ％の範囲
内とした。Cu: Like Mg, Cu itself contributes to solid solution strengthening, and when it coexists with Mg, it strengthens the Al2
It contributes to age hardening due to the precipitation of CuMg, and the above-mentioned effects are particularly great in applications where baking coating is applied, such as lid materials, as in the present invention, and a material with high strength can be obtained after baking coating. If the amount of Cu is less than 0.05 wt%, the effect will be small, and if it exceeds 0.5 wt%, age hardening can be easily obtained, but it will become too hard and disadvantageous for subsequent molding, so the amount of Cu should be 0.05~ It was set within the range of 0.5 wt%.
【００１６】Ｓｉ：ＳｉはＭｇとの共存によりＭｇ２
Ｓｉを析出して時効硬化に寄与するが、この発明の場合
にはそれよりもむしろ、ＦｅおよびＭｎとの共存下で金
属間化合物の適切な分散状態を得るために寄与する。Ｓ
ｉ量が０．１ｗｔ％未満ではその効果が少なく、一方０
．５ｗｔ％を越えればその効果が飽和し、さらにはＭｇ
２ Ｓｉによる時効硬化が過度となったりＳｉ自体によ
る固溶硬化が進んで成形性を悪化させる。したがってＳ
ｉ量は０．１〜０．５ｗｔ％の範囲内とした。Si: Si coexists with Mg, resulting in Mg2
Although Si precipitates and contributes to age hardening, in the case of the present invention, it rather contributes to obtaining an appropriate dispersion state of the intermetallic compound in coexistence with Fe and Mn. S
If the amount of i is less than 0.1 wt%, the effect is small;
．． If it exceeds 5wt%, the effect will be saturated, and even Mg
2 Age hardening due to Si becomes excessive or solid solution hardening due to Si itself progresses, deteriorating formability. Therefore S
The amount of i was within the range of 0.1 to 0.5 wt%.
【００１７】Ｍｎ：Ｍｎは強度向上に寄与するばかりで
なく、この発明において金属間化合物を生成させるため
に必須の元素であり、適切な金属間化合物分散状態を得
るためにＦｅとともに重要な役割を果たす。この発明で
適用される連続鋳造圧延法の如く、冷却速度が速い鋳造
法の場合、Ｍｎ量が２．０ｗｔ％を越えれば、ＭｎＡｌ
６ の初晶巨大金属間化合物を形成して、著しく成形性
を損なう。一方Ｍｎ量が０．５ｗｔ％未満では、必要な
金属間化合物分散状態を得るだけの金属間化合物量を確
保することが困難となる。したがってＭｎ量は０．５〜
２．０ｗｔ％の範囲内とした。Mn: Mn not only contributes to strength improvement, but is also an essential element for generating intermetallic compounds in this invention, and plays an important role together with Fe to obtain an appropriate intermetallic compound dispersion state. Fulfill. In the case of a casting method with a fast cooling rate, such as the continuous casting and rolling method applied in this invention, if the Mn amount exceeds 2.0 wt%, MnAl
6, forming a primary crystal giant intermetallic compound, which significantly impairs formability. On the other hand, if the amount of Mn is less than 0.5 wt%, it becomes difficult to secure an amount of intermetallic compounds sufficient to obtain the required intermetallic compound dispersion state. Therefore, the amount of Mn is 0.5~
It was set within the range of 2.0 wt%.
【００１８】Ｆｅ：ＦｅはＭｎとともに適切な金属間化
合物分散状態を得るために必要な元素であり、しかもＳ
ｉと同様にＭｎの晶出を促進させる元素である。Ｆｅ量
が０．１ｗｔ％未満ではその効果が少なく、一方１．０
ｗｔ％を越えればＭｎ添加と相俟って初晶巨大金属間化
合物を生成して、成形性を損なう。したがってＦｅ量は
０．１〜１．０ｗｔ％の範囲内とした。Fe: Fe, together with Mn, is an element necessary to obtain an appropriate dispersion state of intermetallic compounds.
Like i, it is an element that promotes crystallization of Mn. When the amount of Fe is less than 0.1 wt%, the effect is small;
If it exceeds wt%, a primary crystal giant intermetallic compound is generated together with the addition of Mn, impairing formability. Therefore, the amount of Fe was set within the range of 0.1 to 1.0 wt%.
【００１９】Ｍｎ＋Ｆｅ：Ｍｎ量、Ｆｅ量は個別的には
前述の通りであるが、金属間化合物の生成には両者が並
存することが必要であるから、引き裂き性向上のために
金属間化合物の適切な分散状態を得るためには、両者の
合計含有量も考慮する必要がある。Ｍｎ＋Ｆｅの合計量
が１．０ｗｔ％未満では金属間化合物の適切な分散状態
が得られず、一方その合計量が３．０ｗｔ％を越えれば
初晶金属間化合物を生成して成形性を劣化させる。そこ
でＭｎ＋Ｆｅの合計量を１．０〜３．０ｗｔ％の範囲内
とした。Mn+Fe: The amount of Mn and the amount of Fe are individually as described above, but since it is necessary for both to coexist in order to generate an intermetallic compound, it is necessary to increase the amount of Mn and Fe in order to improve tearability. In order to obtain an appropriate dispersion state, it is necessary to consider the total content of both. If the total amount of Mn + Fe is less than 1.0 wt%, an appropriate dispersion state of intermetallic compounds cannot be obtained, while if the total amount exceeds 3.0 wt%, primary crystal intermetallic compounds are generated and formability is deteriorated. . Therefore, the total amount of Mn+Fe was set within the range of 1.0 to 3.0 wt%.
【００２０】なお通常のアルミニウム合金においては、
鋳塊結晶粒微細化のため、Ｔｉ単独あるいはＴｉをＢと
組合せて微量添加することがあり、この発明でも微量の
Ｔｉ、あるいはＴｉおよびＢを添加することは許容され
る。但しＴｉを添加する場合その添加量が０．０１ｗｔ
％未満では鋳塊結晶粒微細化の効果が得られず、一方０
．３ｗｔ％を越えれば成形性を害するから、Ｔｉは０．
０１〜０．３ｗｔ％の範囲内とすることが好ましい。ま
たＴｉとともにＢを添加する場合、Ｂが１ｐｐｍ 未満
ではその効果がなく、一方５００ｐｐｍを越えれば成形
性を害するからＢは１〜５００ｐｐｍ の範囲内とする
ことが好ましい。[0020] In ordinary aluminum alloys,
In order to refine the ingot crystal grains, a small amount of Ti alone or in combination with B may be added, and the addition of a small amount of Ti or Ti and B is also allowed in this invention. However, when adding Ti, the amount added is 0.01wt.
%, the effect of refining the ingot crystal grains cannot be obtained;
．． If it exceeds 3 wt%, moldability will be impaired, so Ti should be 0.
It is preferably within the range of 0.01 to 0.3 wt%. Furthermore, when B is added together with Ti, if B is less than 1 ppm, there is no effect, while if it exceeds 500 ppm, the moldability is impaired, so B is preferably within the range of 1 to 500 ppm.
【００２１】またこのほか、Ｃｒ，Ｚｒ，Ｖはいずれも
それぞれ０．３ｗｔ％程度までであれば、この発明の効
果を失わずに強度向上に寄与する。またＺｎも０．５ｗ
ｔ％程度までであれば、この発明の効果を失わずに強度
向上に寄与する。[0021] In addition, if each of Cr, Zr, and V is up to about 0.3 wt%, they contribute to improving the strength without losing the effects of the present invention. Also, Zn is 0.5w
If it is up to about t%, it contributes to improving the strength without losing the effect of the present invention.
【００２２】ここで、この発明で規定している合金成分
組成は、２ピースアルミニウム缶の胴材として従来から
広く使用されている３００４合金の成分組成（Ｍｇ０．
８〜１．３ｗｔ％、Ｍｎ１．０〜１．５ｗｔ％、Ｓｉ０
．３０ｗｔ％以下、Ｆｅ０．７ｗｔ％以下、Ｃｕ０．２
５ｗｔ％以下、残部Ａｌ）に近い。そのため、この発明
の製造方法で得られたアルミニウム合金板を蓋材とし、
かつその蓋材を従来の一般的な３００４合金からなる胴
材とを組合せて２ピース缶を作り、その缶をリサイクル
のために回収して再溶解し、その鋳塊（再生塊）から再
び同じ蓋材、胴材を製造する場合には、再溶解時の酸化
によるＭｇのロス（Ｍｇが約２０％減る）を見込んで、
Ｍｇの添加のみを行なえば良く、したがって特に純アル
ミニウムの新地金を添加する必要がないから、リサイク
ルは容易である。ちなみに、蓋材と胴材とを全く同じ合
金で作ってユニアロイ化した場合でも、再溶解時のＭｇ
ロスにより新たなＭｇの添加を行なわなければならない
のが通常であり、したがってこの発明の成分組成範囲内
の合金を蓋材に用いた場合のリサイクルの容易さは、ユ
ニアロイ化した場合と同等と言える。The alloy composition defined in this invention is the composition of 3004 alloy (Mg0.
8-1.3wt%, Mn1.0-1.5wt%, Si0
．． 30wt% or less, Fe0.7wt% or less, Cu0.2
5 wt% or less, the balance is close to Al). Therefore, using the aluminum alloy plate obtained by the manufacturing method of this invention as a lid material,
Then, a two-piece can is made by combining the lid material with a body material made of a conventional general 3004 alloy, and the can is collected and remelted for recycling, and the same ingot is reused from the ingot (regenerated ingot). When manufacturing lid and body materials, take into account the loss of Mg (about 20% reduction in Mg) due to oxidation during remelting.
Recycling is easy because only Mg needs to be added, and there is no need to add new pure aluminum metal. By the way, even if the lid material and the body material are made from the same alloy and made into a unialloy, the Mg during remelting
Normally, new Mg must be added due to loss, so when an alloy within the composition range of this invention is used for the lid material, it can be said that the ease of recycling is equivalent to when it is made into a unialloy. .
【００２３】この発明の成形用アルミニウム合金硬質板
の製造方法においては、上述のように合金成分組成を規
定するだけではなく、金属間化合物の分散状態を適切に
調整することが極めて重要である。In the method of manufacturing a hard aluminum alloy plate for forming according to the present invention, it is extremely important not only to specify the alloy component composition as described above, but also to appropriately adjust the dispersion state of the intermetallic compound.
【００２４】すなわち一般に引き裂き性は、板表面にお
ける金属間化合物の量が多いほど、また金属間化合物の
径が大きいほど良好となる。但し、この発明の方法のよ
うに冷却速度が速い鋳造法を適用して金属間化合物の径
が小さくなっている場合でも、その数が多くなれば引き
裂き荷重は小さくなり、良好な引き裂き性が得られる。
ここで、１μｍ以上の径の金属間化合物の平均径が１．
０〜２．５μｍの場合、その１μｍ以上の径の金属間化
合物の数が、板表面において０．２ｍｍ２ 当り３００
０個未満では、この発明で目標とする程度の優れた引き
裂き性が得られず、したがって１μｍ以上の径の金属間
化合物の平均径が１．０〜２．５μｍの場合、その１μ
ｍ以上の径の金属間化合物の数を０．２ｍｍ２ 当り３
０００個以上とする必要がある。一方金属間化合物の最
大径が１０μｍを越えれば、成形性が低下し、特に蓋材
でディップル部やリベット部に要求される局部的な張り
出し性が低下するから、板表面における金属間化合物最
大径は１０μｍ以下とする必要がある。但しこの発明の
方法では鋳造時の冷却速度が速いため、従来のＤＣ鋳造
法（半連続鋳造法）を適用した場合よりも金属間化合物
径は小さくなり、したがって金属間化合物最大径を容易
に１０μｍ以下とすることができる。なお、冷却速度の
低いＤＣ鋳造法を適用した場合は、金属間化合物の平均
径が３μｍ程度以上と大きく、この場合は１μｍ以上の
金属間化合物の数が１０００個／０．２ｍｍ２ 程度で
も引き裂き性はある程度良好となるが、金属間化合物径
が大きいために、局部的な張り出し性に劣ることになる
。That is, in general, the tearability becomes better as the amount of intermetallic compounds on the plate surface increases and as the diameter of the intermetallic compounds increases. However, even when the diameter of the intermetallic compounds is reduced by applying a casting method with a fast cooling rate, as in the method of this invention, the tearing load decreases as the number of intermetallic compounds increases, resulting in good tearability. It will be done. Here, the average diameter of the intermetallic compound having a diameter of 1 μm or more is 1.
In the case of 0 to 2.5 μm, the number of intermetallic compounds with a diameter of 1 μm or more is 300 per 0.2 mm2 on the plate surface.
If the number is less than 0, the excellent tearability targeted by this invention cannot be obtained. Therefore, if the average diameter of the intermetallic compound with a diameter of 1 μm or more is 1.0 to 2.5 μm, the 1 μm
The number of intermetallic compounds with a diameter of m or more is 3 per 0.2 mm2.
000 or more. On the other hand, if the maximum diameter of the intermetallic compound exceeds 10 μm, the formability will decrease, especially the local extrusion required for the dip and rivet parts of the lid material, so the maximum diameter of the intermetallic compound on the plate surface will decrease. must be 10 μm or less. However, in the method of this invention, the cooling rate during casting is fast, so the diameter of the intermetallic compound is smaller than when applying the conventional DC casting method (semi-continuous casting method), and therefore the maximum diameter of the intermetallic compound can be easily reduced to 10 μm. It can be as follows. In addition, when the DC casting method with a low cooling rate is applied, the average diameter of the intermetallic compounds is large, about 3 μm or more, and in this case, even if the number of intermetallic compounds of 1 μm or more is about 1000 pieces/0.2 mm2, the tearability will be low. However, since the intermetallic compound diameter is large, local extrusion properties are poor.
【００２５】次にこの発明における製造プロセスを説明
する。Next, the manufacturing process in this invention will be explained.
【００２６】先ず前述のような成分組成の合金溶湯を常
法に従って溶製し、５０℃／ｓｅｃ 以上の冷却速度で
厚さ１５ｍｍ以下の薄板に鋳造する。ここで、冷却速度
が最も遅い位置でもその冷却速度が５０℃／ｓｅｃ よ
り遅くなれば、金属間化合物が粗大化するために、成形
性、特に局部張り出し性が悪くなる。また、鋳造板厚が
１５ｍｍより厚ければ、通常の量産的規模での製造にお
いて５０℃／ｓｅｃ 以上の高い冷却速度を得ることが
困難となるから、鋳造板厚は１５ｍｍ以下と規定した。
なおこのような冷却速度を実操業上で実現するためには
、連続鋳造圧延法（薄板連続鋳造法）等の所謂連続鋳造
法を適用すれば良い。[0026] First, a molten alloy having the above-mentioned composition is melted according to a conventional method and cast into a thin plate having a thickness of 15 mm or less at a cooling rate of 50° C./sec or more. Here, if the cooling rate is slower than 50° C./sec even at the position where the cooling rate is slowest, the intermetallic compound becomes coarse and the formability, especially local extrusion properties, deteriorates. Furthermore, if the thickness of the cast plate is thicker than 15 mm, it will be difficult to obtain a high cooling rate of 50° C./sec or more in normal mass production, so the thickness of the cast plate is specified to be 15 mm or less. In order to realize such a cooling rate in actual operation, a so-called continuous casting method such as a continuous casting and rolling method (thin plate continuous casting method) may be applied.
【００２７】このようにして得られた薄板（連続鋳造板
）に対しては、直ちに１次冷間圧延を施して所要の中間
板厚とする（請求項１の方法）か、または均熱処理を施
してから１次冷間圧延を施して所要の板厚とする（請求
項２の方法）。またここで１次冷間圧延は、中途に焼鈍
を挟む２回以上の圧延に分けて行なっても良い（請求項
３の方法）。The thus obtained thin plate (continuously cast plate) is immediately subjected to primary cold rolling to obtain the required intermediate plate thickness (method according to claim 1), or subjected to soaking treatment. After that, the plate is subjected to primary cold rolling to obtain a required thickness (method according to claim 2). Moreover, here, the primary cold rolling may be performed in two or more rolling steps with annealing in between (method according to claim 3).
【００２８】ここで、１次冷間圧延に均熱処理を施して
おけば、金属間化合物が丸味を帯びるとともに、Ａｌマ
トリックス中の合金元素の濃度が均一となり、これによ
って成形性向上に寄与する。この均熱化処理は、３００
〜６３０℃の範囲内の温度に加熱して１時間以上保持す
る条件とする。均熱温度が３００℃未満では上述の効果
が得られず、一方６３０℃を越える高温では部分的な融
解が開始されてしまう。また均熱時間が１時間未満でも
均熱効果が得られない。[0028] Here, if a soaking treatment is performed during the primary cold rolling, the intermetallic compound becomes rounded and the concentration of alloying elements in the Al matrix becomes uniform, thereby contributing to improved formability. This soaking treatment is performed at a temperature of 300
The conditions are to heat to a temperature within the range of ~630°C and hold for 1 hour or more. If the soaking temperature is less than 300°C, the above-mentioned effect cannot be obtained, while if the soaking temperature is higher than 630°C, partial melting will start. Further, even if the soaking time is less than 1 hour, the soaking effect cannot be obtained.
【００２９】また１次冷間圧延を、中途に焼鈍を挟む２
回以上の圧延に分けて行なう場合、その焼鈍は、１次冷
間圧延後の中間焼鈍と同様な急速加熱、急速冷却の高温
短時間保持とする。具体的には、１℃／ｓｅｃ 以上の
昇温速度で５００〜６００℃の範囲内の温度に加熱し、
その範囲内の温度に到達後、直ちに、または１２０秒以
下の保持後１℃／ｓｅｃ 以上の冷却速度で冷却する。
この発明で対象としている材料の場合、Ｍｎ固溶量が多
いが、上述のような１次冷間圧延中途での焼鈍はＭｎの
析出を防止して、最終板の強度向上に寄与する。一方こ
の焼鈍では、Ｆｅ固溶量は減るが、これは耳率の点から
は不利となる。この焼鈍が前述のような条件を外れれば
、上述のような効果が得られない。なおこのような急速
加熱・急速冷却、高温短時間保持の焼鈍条件は、コイル
を連続的に巻戻しながら行なう所謂連続焼鈍によって達
成できる。なおまた、上述のように中途で焼鈍を挟んで
１次冷間圧延を行なう場合、その１次冷間圧延における
最終の圧延は、圧延率を２５％以上とすることが望まし
い。[0029] In addition, the first cold rolling is performed by inserting annealing in the middle.
When rolling is carried out in multiple rounds or more, the annealing is carried out at a high temperature for a short period of time with rapid heating and rapid cooling, similar to the intermediate annealing after the primary cold rolling. Specifically, heating to a temperature within the range of 500 to 600 °C at a temperature increase rate of 1 °C/sec or more,
After reaching the temperature within this range, it is cooled immediately or at a cooling rate of 1° C./sec or more after being maintained for 120 seconds or less. In the case of the material targeted by this invention, the amount of solid solution of Mn is large, but the above-mentioned annealing in the middle of the primary cold rolling prevents precipitation of Mn and contributes to improving the strength of the final plate. On the other hand, in this annealing, the amount of Fe solid solution decreases, but this is disadvantageous in terms of the selvage ratio. If this annealing does not meet the above-mentioned conditions, the above-mentioned effects cannot be obtained. Note that such annealing conditions such as rapid heating, rapid cooling, and holding at high temperature for a short time can be achieved by so-called continuous annealing in which the coil is continuously unwound. Furthermore, when primary cold rolling is performed with intermediate annealing as described above, it is desirable that the final rolling in the primary cold rolling has a rolling rate of 25% or more.
【００３０】以上のようにして１次冷間圧延を施して所
要の中間板厚とした板に対しては、急速加熱・急速冷却
、高温短時間保持の中間焼鈍を行なう。具体的には、１
℃／ｓｅｃ 以上の昇温速度で加熱して４５０〜６００
℃の範囲内の温度に到達させ、その範囲内の温度に到達
後、直ちにもしくは１２０秒以内の保持後、１℃／ｓｅ
ｃ 以上の冷却速度で冷却する。この中間焼鈍は、Ｃｕ
，Ｍｇ，Ｓｉ等の固溶を繰返して、溶体化効果により焼
付塗装後の強度を維持するために必要な工程である。こ
こで、１次中間焼鈍の昇温速度、冷却速度が１℃／ｓｅ
ｃ 未満では、固溶したＭｎ，Ｃｕ，Ｍｇ，Ｓｉ等が逆
に析出してしまうから、昇温速度、冷却速度はともに１
℃／ｓｅｃ 以上とする必要がある。また加熱到達温度
が４５０℃未満ではＣｕ，Ｍｇ，Ｓｉ等の元素を充分に
固溶させることができず、一方６００℃を越えるような
高温は通常の量産的規模でのラインでは得難い。さらに
、保持時間が１２０秒を越えれば表面酸化が進行して外
観不良が発生するおそれがある。したがって中間焼鈍の
各条件は前述のように定めた。なおこのような中間焼鈍
条件は、前記同様に所謂連続焼鈍によって達成できる。[0030] The plate subjected to primary cold rolling as described above to obtain a required intermediate plate thickness is subjected to rapid heating, rapid cooling, and intermediate annealing by holding at high temperature for a short time. Specifically, 1
Heating at a temperature increase rate of ℃/sec or more to 450-600
After reaching the temperature within the range of ℃, immediately or after holding within 120 seconds, 1℃/se
Cool at a cooling rate of c or more. This intermediate annealing is performed using Cu
, Mg, Si, etc., and is necessary to maintain the strength after baking coating due to the solution treatment effect. Here, the heating rate and cooling rate of the primary intermediate annealing are 1°C/sec.
If the temperature is less than c, solid solution Mn, Cu, Mg, Si, etc. will precipitate, so the heating rate and cooling rate will both be 1.
It is necessary to set it to ℃/sec or more. Further, if the heating temperature reached is less than 450°C, elements such as Cu, Mg, Si, etc. cannot be sufficiently solid-dissolved, and on the other hand, high temperatures exceeding 600°C are difficult to obtain on a normal mass production scale line. Furthermore, if the holding time exceeds 120 seconds, surface oxidation may progress and poor appearance may occur. Therefore, the conditions for intermediate annealing were determined as described above. Note that such intermediate annealing conditions can be achieved by so-called continuous annealing as described above.
【００３１】以上のようにして中間焼鈍を施した後には
、製品板厚まで最終冷間圧延を施す。このときの冷間圧
延率は３０％以上であれば、成分組成や他のプロセス条
件を適切に選定することにより所要の高強度が得られる
。After performing the intermediate annealing as described above, final cold rolling is performed to the thickness of the product plate. If the cold rolling rate at this time is 30% or more, the required high strength can be obtained by appropriately selecting the component composition and other process conditions.
【００３２】最終冷間圧延によって得られた最終板厚の
圧延板は、これをそのまま蓋材として缶蓋に供しても良
いが、１００〜２００℃の範囲内の温度で３０分から１
０時間程度の最終焼鈍を施せば、時効析出を促進させて
、焼付塗装における強度低下を少なくすることができ、
同じ成分組成、同じ製造プロセス条件でもより高強度の
蓋材を得ることが可能となる。またこのように最終焼鈍
により強度向上が図られるため、最終的な強度が同じで
も最終冷間圧延率を下げることができ、そのため成形性
や耳率は良好となる。[0032] The rolled plate having the final thickness obtained by the final cold rolling may be used as a lid material for can lids.
If final annealing is performed for about 0 hours, aging precipitation can be promoted and strength loss during baking coating can be reduced.
Even with the same component composition and the same manufacturing process conditions, it is possible to obtain a lid material with higher strength. Further, since the final annealing improves the strength in this way, the final cold rolling rate can be lowered even if the final strength is the same, and therefore the formability and edge ratio are improved.
【００３３】以上のように、合金成分組成条件、各プロ
セス条件（特に鋳造条件と中間焼鈍条件）、および最終
板での金属間化合物分散条件を適切に定めることによっ
て、従来２ピース缶胴材に用いられていた３００４合金
よりも格段に高い強度を有し、かつ従来２ピース缶蓋材
として用いられていた５１８２合金と同程度の高強度を
有するばかりでなく、従来の５１８２合金と比較して格
段に引き裂き性に優れ、そのほか成形性（特に局部張り
出し性）にも優れたアルミニウム合金硬質板を得ること
が可能となったのである。したがってこの発明の方法に
より得られるアルミニウム合金硬質板は、２ピース缶の
蓋材、特に引き裂き性が良好であることが要求されるス
テイオンタブ方式の蓋材に最適であるが、この発明の方
法によるアルミニウム合金硬質板の成分組成は従来から
胴材として使用されている３００４合金の成分組成に近
いため、２ピース缶蓋材に使用すれば、缶胴材に近い成
分組成となり、その結果アルミニウム２ピース缶のリサ
イクルを容易化することができる。また缶胴材に同じ成
分組成の合金板を用いて２ピース缶のユニアロイ化を図
り、より一層のリサイクル容易化を図ることも可能であ
る。なおこの発明の方法により得られた硬質板は、ステ
イオンタブ方式の缶蓋に限らず、プルタブ方式の缶蓋に
も使用し得ることはもちろんである。As described above, by appropriately determining the alloy composition conditions, each process condition (especially casting conditions and intermediate annealing conditions), and the intermetallic compound dispersion conditions in the final plate, it is possible to improve the conventional two-piece can body material. It not only has much higher strength than the 3004 alloy that was used, and has the same high strength as the 5182 alloy that was conventionally used as a two-piece can lid material, but also has a higher strength than the conventional 5182 alloy. It has now become possible to obtain an aluminum alloy hard plate that has extremely good tearability and also has excellent formability (particularly local stretchability). Therefore, the aluminum alloy hard plate obtained by the method of the present invention is most suitable for two-piece can lids, especially for stay-on tab type lids that require good tearability. The composition of the aluminum alloy hard plate is close to that of 3004 alloy, which has traditionally been used as a body material, so if it is used for a two-piece can lid material, the composition will be close to that of the can body material, and as a result, aluminum 2 Recycling of peace cans can be facilitated. It is also possible to make a two-piece can into a unialloy by using an alloy plate with the same composition as the can body material, thereby making it even easier to recycle. It goes without saying that the hard plate obtained by the method of the present invention can be used not only for stay-on tab type can lids but also for pull tab type can lids.
【００３４】[0034]
【実施例】表１の合金符号Ａで示すこの発明の成分組成
範囲内の合金について、表２の製造番号１〜５に示すよ
うな工程・条件を適用した。また従来の蓋材として用い
られている５１８２合金に相当する表１の合金符号Ｂで
示す合金について、表２の製造番号６に示す工程・条件
を適用した。すなわち、合金Ａについて、製造番号１〜
４の場合は、連続鋳造圧延法を適用して冷却速度１００
℃／ｓｅｃ で連続鋳造し、板厚６ｍｍの鋳造板とし、
その後製造番号１の場合は［均熱処理］→［１次冷間圧
延］→［中間焼鈍］→［最終冷間圧延］→［最終焼鈍］
の順で処理し、製造番号２の場合は均熱処理なしで［１
次冷間圧延］→［中間焼鈍］→［最終冷間圧延］（最終
焼鈍なし）の順で処理し、製造番号３の場合は均熱処理
なしで［中途に焼鈍を挟んだ１次冷間圧延］→［中間焼
鈍］→［最終冷間圧延］→［最終焼鈍］の順で処理し、
さらに製造番号４の場合は均熱処理なしで［１次冷間圧
延］→［中間焼鈍］→［最終冷間圧延］→［最終焼鈍］
の順で処理した。一方合金符号Ａについての製造番号５
の場合、および合金符号Ｂについての製造番号６の場合
は、ＤＣ鋳造法（半連続鋳造法）により冷却速度１０℃
／ｓｅｃ で鋳造し、その鋳塊に対し［均熱処理］→［
熱間圧延］→［１次冷間圧延］→［中間焼鈍］→［最終
冷間圧延］を施し、さらに製造番号５の場合は最終焼鈍
を施し、製造番号６の場合は最終焼鈍なしで仕上げた。
なお、中間焼鈍は連続焼鈍もしくはバッチ式の箱型焼鈍
によって行なったが、連続焼鈍の場合の昇温速度、冷却
速度はいずれも３０℃／ｓｅｃ であり、また箱型焼鈍
の場合の昇温速度、冷却速度はいずれも３５℃／ｈｒで
ある。[Example] The processes and conditions shown in production numbers 1 to 5 in Table 2 were applied to an alloy within the composition range of the present invention shown by alloy code A in Table 1. Further, the process and conditions shown in manufacturing number 6 in Table 2 were applied to the alloy shown by alloy code B in Table 1, which corresponds to the 5182 alloy used as a conventional lid material. That is, for alloy A, manufacturing numbers 1-
In the case of No. 4, the continuous casting and rolling method is applied and the cooling rate is 100.
Continuously cast at ℃/sec to form a cast plate with a thickness of 6 mm,
After that, in the case of production number 1, [Soaking treatment] → [Primary cold rolling] → [Intermediate annealing] → [Final cold rolling] → [Final annealing]
In the case of production number 2, process [1] without soaking treatment.
Next cold rolling]→[Intermediate annealing]→[Final cold rolling] (no final annealing) ]→[Intermediate annealing]→[Final cold rolling]→[Final annealing]
Furthermore, in the case of production number 4, there is no soaking treatment, [first cold rolling] → [intermediate annealing] → [final cold rolling] → [final annealing]
Processed in this order. On the other hand, serial number 5 for alloy code A
, and in the case of manufacturing number 6 for alloy code B, the cooling rate is 10°C by DC casting method (semi-continuous casting method).
/sec, and the ingot is subjected to [soaking treatment] → [
Hot rolling] → [Primary cold rolling] → [Intermediate annealing] → [Final cold rolling], and in the case of serial number 5, final annealing is applied, and in the case of serial number 6, finishing is done without final annealing. Ta. Note that intermediate annealing was performed by continuous annealing or batch type box-type annealing, but the heating rate and cooling rate in the case of continuous annealing were both 30°C/sec, and the heating rate in the case of box-type annealing was 30°C/sec. , the cooling rate was 35°C/hr.
【００３５】以上のようにして得られた各板について、
その表面における１μｍ以上の径の金属間化合物の０．
２ｍｍ２ 当りの個数と平均径、および表面の金属間化
合物の最大径を調べたので、その結果を表３に示す。な
おここで１μｍ以上の金属間化合物の個数および平均径
は、画像解析装置により表面の画像を２値化して０．２
ｍｍ２ 当りの個数分布を求めた。Regarding each plate obtained as above,
of intermetallic compounds with a diameter of 1 μm or more on its surface.
The number of particles per 2 mm2, average diameter, and maximum diameter of intermetallic compounds on the surface were investigated, and the results are shown in Table 3. Note that the number and average diameter of intermetallic compounds of 1 μm or more are determined by binarizing the surface image using an image analysis device and calculating 0.2
The number distribution per mm2 was determined.
【００３６】さらに各板について、連続焼付塗装に相当
する熱処理として、オイルバスによる２７０℃×２０ｓ
ｅｃ の熱処理を施し、この連続焼付塗装相当熱処理後
の板について、圧延方向に対し４５°の方向の耐力（す
なわち一般的に面内各方向のうち耐力値が最低となる方
向の耐力）を調べるとともに、成形性評価として局部張
り出し性を調べ、さらに製缶後の開蓋力を調べたので、
その結果を表３中に示す。Furthermore, each board was subjected to heat treatment equivalent to continuous baking painting at 270°C for 20 seconds in an oil bath.
ec heat treatment, and examine the yield strength in the direction of 45° to the rolling direction (that is, the yield strength in the direction where the yield strength value is generally the lowest among all directions in the plane) for the plate after this heat treatment equivalent to continuous baking painting. At the same time, we investigated local extrusion properties as a formability evaluation, and also investigated the opening force after can manufacturing.
The results are shown in Table 3.
【００３７】なおここで局部張り出し性試験は、直径２
ｍｍ、先端曲率半径１ｍｍの球頭ポンチを用い、ダイス
板上に試験材料板を載置してプレス成形を行ない、かつ
ポンチ長さを１．０ｍｍ〜１．９ｍｍまで０．１ｍｍご
とに１０段階に変化（この１０段階をポンチ長さの短い
方から順にランク１、ランク２、……ランク１０とする
）させ、割れが発生した段階の１段階手前のランクを表
２中に記載した。したがってランクの数値が大きくなる
ほど局部張り出し性は良好となる。さらに製蓋後の開蓋
力については、各板を用いて実際にプルタブ方式の２ピ
ース缶の蓋に成形し、各蓋について開蓋に要する力（荷
重）を「ポップ」、「ティア」、「デタッチ」の３段階
で調べた。
ここで「ポップ」はプルタブ方式のタブを最初に引上げ
てスコアーに亀裂を発生させる際の荷重、また「ティア
」はスコアーに亀裂発生後、スコアーが引き裂かれて行
く過程での最大荷重、「デタッチ」は最後にタブがスコ
アーの開蓋部分とともに蓋から切離される際の荷重をあ
らわす。[0037] Here, the local overhang property test was performed using a diameter of 2
Using a ball-head punch with a tip radius of curvature of 1 mm, press-form the test material plate by placing it on a die plate, and change the punch length from 1.0 mm to 1.9 mm in 10 steps in 0.1 mm increments. (These 10 levels are ranked in order from the shortest punch length to rank 1, rank 2, ... rank 10), and the rank one level before the stage where cracking occurred is listed in Table 2. Therefore, the larger the rank value, the better the local protrusion property becomes. Furthermore, regarding the opening force after making the lid, we actually formed the lid of a two-piece pull-tab can using each plate, and calculated the force (load) required to open each lid by "pop", "tear", We investigated the three stages of ``detach''. Here, "Pop" is the load when the tab of the pull tab method is first pulled up to generate a crack in the score, and "Tear" is the maximum load in the process of tearing the score after a crack occurs in the score, and "Detached"'' represents the load when the tab is finally separated from the lid along with the opening part of the score.
【００３８】[0038]
【表１】[Table 1]
【００３９】[0039]
【表２】[Table 2]
【００４０】[0040]
【表３】[Table 3]
【００４１】表３に示すように、合金成分組成および金
属間化合物分散条件がこの発明で規定する範囲を満たし
かつ製造プロセスもこの発明の範囲を満たしている製造
番号１〜３により得られた板は、いずれも従来の５１８
２合金（製造番号６）と同等以上の耐力を有し、かつ局
部張り出し性が優れるとともに、製蓋後の開蓋力が５１
８２合金の場合よりも格段に少なくて済み、引き裂き性
に優れていることが明らかである。なおここで実施例で
は製蓋後の開蓋力として、プルタブ方式の場合について
調べたが、プルタブ方式での開蓋力、特に「ティア」の
荷重が小さいことは、ステイオンタブ方式でも開蓋力が
小さくて済むことを意味している。As shown in Table 3, the plates obtained by production numbers 1 to 3 whose alloy component composition and intermetallic compound dispersion conditions meet the ranges specified in the present invention, and whose manufacturing processes also meet the scope of the present invention. are all conventional 518
It has a yield strength equal to or higher than that of 2 alloy (manufacturing number 6), has excellent local protrusion properties, and has a lid opening force of 51
It is clear that the amount required is significantly less than that of 82 alloy, and that the tear resistance is excellent. In this example, we investigated the case of the pull-tab method as the opening force after making the lid, but the fact that the opening force of the pull-tab method, especially the load on the "tear" is small, means that even the stay-on tab method can be used to open the lid. This means that less force is required.
【００４２】一方製造番号４は、中間焼鈍として徐加熱
・徐冷却の比較的低温長時間の箱型焼鈍を適用した比較
例であるが、この場合には強度が若干低目であるばかり
でなく、局部張り出し性が劣っていた。On the other hand, production number 4 is a comparative example in which box-type annealing at a relatively low temperature and for a long period of time with slow heating and slow cooling was applied as intermediate annealing, but in this case, not only the strength was slightly lower, but also the strength was lower. , local extrusion properties were poor.
【００４３】さらに製造番号５は、凝固速度が遅いＤＣ
鋳造法を適用したものであり、この場合は金属間化合物
の数が１０００個／０．２ｍｍ２ と少ないが、その平
均径が３μｍ、最大径が１２μｍと大きいため、局部張
り出し性が劣っていた。Furthermore, production number 5 is a DC with a slow solidification rate.
A casting method was applied, and in this case, the number of intermetallic compounds was small at 1000 pieces/0.2 mm2, but the average diameter was large, 3 μm, and the maximum diameter was 12 μm, resulting in poor local extrusion properties.
【００４４】さらに製造番号６の場合は、合金として従
来の蓋材に用いられている５１８２合金相当のものを用
い、かつ製造プロセスとしても、従来の一般的なＤＣ鋳
造法を適用したものであり、この場合、金属間化合物の
径は大きいが、その数が著しく少なく、そのため引き裂
き性に劣り、製蓋後の開蓋力として大きな荷重を必要と
した。Furthermore, in the case of serial number 6, an alloy equivalent to 5182 alloy, which is used in conventional lid materials, is used, and the manufacturing process is a conventional general DC casting method. In this case, although the diameter of the intermetallic compound is large, the number of intermetallic compounds is extremely small, so the tearability is poor, and a large load is required as the opening force after the lid is manufactured.
【００４５】[0045]
【発明の効果】前述の実施例からも明らかなように、こ
の発明の製造方法によれば、引き裂き性が優れ、かつ焼
付塗装後の耐力として高い強度を有するとともに成形性
、特に局部張り出し性に優れたアルミニウム合金硬質板
を得ることができる。したがってこの発明の製造方法に
より得られたアルミニウム合金硬質板は、特にアルミニ
ウム缶の蓋材に好適であり、ステイオンタブ方式の缶蓋
材として用いれば、引き裂き性が優れるため飲み口部分
をスコアーから均一かつ容易に引き裂くことができ、開
缶の失敗を招くおそれが少なく、また焼付塗装後に高強
度を有するため、缶体の薄肉化に充分に対応することが
できる。またこの発明の製造方法により得られたアルミ
ニウム合金硬質板は、その成分組成が従来からアルミニ
ウム缶の胴材として使用されている３００４合金に近い
ため、これを蓋材として３００４合金胴材と組合せるこ
とにより、アルミニウム缶のリサイクルの容易化を図る
ことができる。[Effects of the Invention] As is clear from the above-mentioned examples, the manufacturing method of the present invention has excellent tearability and high strength as a proof stress after baking coating, as well as good formability, especially local bulgeability. An excellent aluminum alloy hard plate can be obtained. Therefore, the aluminum alloy hard plate obtained by the manufacturing method of the present invention is particularly suitable for the lid material of aluminum cans, and when used as the can lid material of the stay-on tab method, it has excellent tearability and can be easily removed from the drinking spout from the score. It can be torn uniformly and easily, there is little risk of failure in opening the can, and it has high strength after baking, so it can fully cope with thinning of the can body. Furthermore, since the aluminum alloy hard plate obtained by the manufacturing method of the present invention has a composition similar to that of 3004 alloy, which has been conventionally used as the body material of aluminum cans, this can be combined with the 3004 alloy body material as a lid material. By doing so, recycling of aluminum cans can be facilitated.
【図１】ステイオンタブ方式の缶における缶蓋上面を示
す平面図である。FIG. 1 is a plan view showing the top surface of a can lid of a stay-on tab type can.
【図２】ステイオンタブ方式の缶における缶蓋上面の縦
断面図、すなわち図１のＡ−Ａ線における縦断面図であ
る。FIG. 2 is a vertical cross-sectional view of the top surface of the can lid of a stay-on tab type can, that is, a vertical cross-sectional view taken along line A-A in FIG. 1;
【図３】ステイオンタブ方式の缶における開缶時の缶蓋
上面の状態を図２に対応して示す縦断面図である。FIG. 3 is a longitudinal cross-sectional view corresponding to FIG. 2, showing the state of the top surface of the can lid of a stay-on tab type can when the can is opened.
Claims (4)
０５〜０．５ｗｔ％、Ｍｎ０．５〜２．０ｗｔ％、Ｆｅ
０．１〜１．０ｗｔ％、Ｓｉ０．１〜０．５ｗｔ％を含
有し、かつＦｅとＭｎの合計含有量が１．０〜３．０ｗ
ｔ％の範囲内にあり、残部がＡｌおよび不可避的不純物
よりなる合金を、５０℃／ｓｅｃ 以上の冷却速度で厚
さ１５ｍｍ以下の薄板に鋳造し、その後所要の中間板厚
まで１次冷間圧延を施した後、１℃／ｓｅｃ 以上の昇
温速度で４５０〜６００℃の範囲内の温度に加熱して直
ちにもしくは１２０ｓｅｃ 以下の短時間保持後、１℃
／ｓｅｃ 以上の冷却速度で冷却する中間焼鈍を施し、
さらに３０％以上の圧延率で最終冷間圧延を施し、これ
によって表面における１．０μｍ以上の金属間化合物の
数が０．２ｍｍ２ 当り３０００個以上でかつその平均
径が１．０〜２．５μｍの範囲内にあり、しかも表面に
おける金属間化合物の最大径が１０μｍ以下である板を
得ることを特徴とする、引き裂き性に優れた成形用アル
ミニウム合金硬質板の製造方法。Claim 1: Mg1.0-3.0wt%, Cu0.
05-0.5wt%, Mn0.5-2.0wt%, Fe
0.1 to 1.0 wt%, Si 0.1 to 0.5 wt%, and the total content of Fe and Mn is 1.0 to 3.0 w.
t%, with the remainder consisting of Al and unavoidable impurities, is cast into a thin plate with a thickness of 15 mm or less at a cooling rate of 50°C/sec or more, and then subjected to primary cold rolling to the required intermediate plate thickness. After rolling, heat to a temperature within the range of 450 to 600°C at a temperature increase rate of 1°C/sec or more and immediately or after holding for a short time of 120 seconds or less, 1°C
Perform intermediate annealing by cooling at a cooling rate of /sec or more,
Furthermore, final cold rolling is performed at a rolling rate of 30% or more, so that the number of intermetallic compounds of 1.0 μm or more on the surface is 3000 or more per 0.2 mm2 and the average diameter is 1.0 to 2.5 μm. A method for producing an aluminum alloy hard plate for forming with excellent tearability, characterized by obtaining a plate in which the maximum diameter of intermetallic compounds on the surface is within the range of 10 μm or less.
鋳造と前記１次冷間圧延との間に、さらに３００〜６３
０℃の範囲内の温度に１時間以上保持する均熱処理を行
なう、引き裂き性に優れた成形用アルミニウム合金硬質
板の製造方法。2. The method according to claim 1, wherein between the casting and the primary cold rolling, a rolling stock of 300 to 63
A method for producing a hard aluminum alloy plate for forming with excellent tearability, which comprises performing soaking treatment at a temperature within the range of 0°C for 1 hour or more.
において、前記１次冷間圧延の中途で、１℃／ｓｅｃ
以上の加熱速度で５００〜６００℃の範囲内の温度に加
熱して直ちにもしくは１２０ｓｅｃ 以下の短時間保持
後１℃／ｓｅｃ 以上の冷却速度で冷却する焼鈍を施す
、引き裂き性に優れた成形用アルミニウム合金硬質板の
製造方法。3. In the method according to claim 1 or 2, in the middle of the first cold rolling, the rolling process is performed at a rate of 1°C/sec.
Forming aluminum with excellent tearability, which is annealed by heating to a temperature in the range of 500 to 600°C at a heating rate of 500 to 600°C, or holding it for a short time of 120 seconds or less, and then cooling at a cooling rate of 1°C/sec or more. Method for manufacturing hard alloy plates.
の方法において、前記最終冷間圧延の後、さらに１０〜
１００℃／ｈｒの昇温速度で１２０〜２００℃の範囲内
の温度に加熱して３０分以上保持しさらに１０〜１００
℃／ｈｒの冷却速度で冷却する最終焼鈍を施す、引き裂
き性に優れた成形用アルミニウム合金硬質板の製造方法
。4. The method according to claim 1, wherein after the final cold rolling, further 10 to
Heat to a temperature within the range of 120 to 200 °C at a heating rate of 100 °C/hr, hold for 30 minutes or more, and then heat to a temperature of 10 to 100 °C.
A method for manufacturing an aluminum alloy hard plate for forming with excellent tearability, which performs final annealing by cooling at a cooling rate of °C/hr.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12290191A JPH04325659A (en) | 1991-04-26 | 1991-04-26 | Manufacture of aluminum alloy hard sheet for forming excellent in tearing property |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12290191A JPH04325659A (en) | 1991-04-26 | 1991-04-26 | Manufacture of aluminum alloy hard sheet for forming excellent in tearing property |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04325659A true JPH04325659A (en) | 1992-11-16 |
Family
ID=14847425
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP12290191A Withdrawn JPH04325659A (en) | 1991-04-26 | 1991-04-26 | Manufacture of aluminum alloy hard sheet for forming excellent in tearing property |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04325659A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06316739A (en) * | 1993-04-28 | 1994-11-15 | Kobe Steel Ltd | Al alloy sheet for negative pressure can stay on tab type end, excellent in can openability, and its production |
| WO1999013118A1 (en) * | 1997-09-11 | 1999-03-18 | Nippon Light Metal Company Ltd. | Aluminum alloy sheet for spot welding |
| JP2005307300A (en) * | 2004-04-23 | 2005-11-04 | Nippon Light Metal Co Ltd | Al-Mg ALLOY SHEET HAVING EXCELLENT HIGH TEMPERATURE HIGH SPEED FORMABILITY AND ITS PRODUCTION METHOD |
| JP2017008388A (en) * | 2015-06-24 | 2017-01-12 | 株式会社神戸製鋼所 | Aluminum alloy sheet for can top |
-
1991
- 1991-04-26 JP JP12290191A patent/JPH04325659A/en not_active Withdrawn
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06316739A (en) * | 1993-04-28 | 1994-11-15 | Kobe Steel Ltd | Al alloy sheet for negative pressure can stay on tab type end, excellent in can openability, and its production |
| WO1999013118A1 (en) * | 1997-09-11 | 1999-03-18 | Nippon Light Metal Company Ltd. | Aluminum alloy sheet for spot welding |
| US6369347B1 (en) | 1997-09-11 | 2002-04-09 | Nippon Light Metal Company, Ltd. | Aluminum alloy sheet for spot welding |
| CN1097096C (en) * | 1997-09-11 | 2002-12-25 | 日本轻金属株式会社 | Aluminum alloy sheet for spot welding |
| KR100564077B1 (en) * | 1997-09-11 | 2006-03-27 | 니폰 라이트 메탈 컴퍼니 리미티드 | Aluminum Alloy Sheet For Spot Welding |
| JP2005307300A (en) * | 2004-04-23 | 2005-11-04 | Nippon Light Metal Co Ltd | Al-Mg ALLOY SHEET HAVING EXCELLENT HIGH TEMPERATURE HIGH SPEED FORMABILITY AND ITS PRODUCTION METHOD |
| JP4534573B2 (en) * | 2004-04-23 | 2010-09-01 | 日本軽金属株式会社 | Al-Mg alloy plate excellent in high-temperature high-speed formability and manufacturing method thereof |
| JP2017008388A (en) * | 2015-06-24 | 2017-01-12 | 株式会社神戸製鋼所 | Aluminum alloy sheet for can top |
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| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Application deemed to be withdrawn because no request for examination was validly filed |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 19980711 |