JP4393949B2 - High strength aluminum alloy plate for wide-mouth bottle can cap - Google Patents
High strength aluminum alloy plate for wide-mouth bottle can cap Download PDFInfo
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- JP4393949B2 JP4393949B2 JP2004246947A JP2004246947A JP4393949B2 JP 4393949 B2 JP4393949 B2 JP 4393949B2 JP 2004246947 A JP2004246947 A JP 2004246947A JP 2004246947 A JP2004246947 A JP 2004246947A JP 4393949 B2 JP4393949 B2 JP 4393949B2
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- 229910000838 Al alloy Inorganic materials 0.000 title claims description 21
- 210000005069 ears Anatomy 0.000 claims description 20
- 238000005096 rolling process Methods 0.000 claims description 13
- 238000012360 testing method Methods 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 239000000126 substance Substances 0.000 claims description 6
- 229910052725 zinc Inorganic materials 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 238000007639 printing Methods 0.000 claims description 4
- 238000012545 processing Methods 0.000 claims description 4
- 235000013361 beverage Nutrition 0.000 claims description 3
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 238000010422 painting Methods 0.000 claims description 2
- 239000000463 material Substances 0.000 description 16
- 239000011572 manganese Substances 0.000 description 14
- 238000010438 heat treatment Methods 0.000 description 13
- 238000000137 annealing Methods 0.000 description 12
- 229910045601 alloy Inorganic materials 0.000 description 11
- 239000000956 alloy Substances 0.000 description 11
- 239000013078 crystal Substances 0.000 description 9
- 238000005452 bending Methods 0.000 description 8
- 238000005097 cold rolling Methods 0.000 description 7
- 238000004519 manufacturing process Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 238000000465 moulding Methods 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 5
- 239000002184 metal Substances 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 4
- 230000001965 increasing effect Effects 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 229910018134 Al-Mg Inorganic materials 0.000 description 3
- 229910018467 Al—Mg Inorganic materials 0.000 description 3
- 229910000914 Mn alloy Inorganic materials 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 230000006641 stabilisation Effects 0.000 description 3
- 238000011105 stabilization Methods 0.000 description 3
- 229910000861 Mg alloy Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 239000000523 sample Substances 0.000 description 2
- 229910018084 Al-Fe Inorganic materials 0.000 description 1
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 229910018575 Al—Ti Inorganic materials 0.000 description 1
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- -1 aluminum-magnesium-manganese Chemical compound 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000012733 comparative method Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000005238 degreasing Methods 0.000 description 1
- 230000000994 depressogenic effect Effects 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000002210 silicon-based material Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
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Description
本発明は、広口ボトル缶用のPP(pilfer proof)キャップに好適に使用されるAl−Mg−Mn(アルミニウム−マグネシウム−マンガン)系合金板に関するものである。 The present invention relates to an Al—Mg—Mn (aluminum-magnesium-manganese) based alloy plate suitably used for a PP (pilfer proof) cap for a wide-mouth bottle can.
PPキャップは、一般に、素材であるアルミニウム合金板に塗装・印刷を施してから、複数の円筒状のカップを同時に成形し、各カップの耳部をトリミングした後、裾部にミシン目を加工するという工程で製造する。こうして成形されたキャップは、飲料容器に内容物を充填後、その容器のネジ部に巻締めされ、市場に出される。 PP caps are generally coated and printed on an aluminum alloy plate that is a material, then a plurality of cylindrical cups are formed at the same time, the ears of each cup are trimmed, and perforations are processed in the hem. It is manufactured by the process. The cap formed in this way is filled with the contents in the beverage container, wound around the threaded portion of the container, and put on the market.
これまで、直径28mm以下の小口のPPキャップには、主にAl−Mn系の3105合金(特許文献1参照)、あるいはAl−Fe系の8011合金が使われていた(非特許文献1参照)。一方、直径38mm等の広口キャップには、強度がより高い必要性があることから、Al−Mg系の5151合金(Al−1.5〜2.1%Mg合金)が使われている。しかし、より高内圧のかかる内容物に対して、あるいはゲージダウン(板厚の減少)に対しては、より高強度でかつ開栓性の良い板が期待されている。 Until now, Al-Mn 3105 alloy (see Patent Document 1) or Al-Fe 8011 alloy has been mainly used for PP caps with a diameter of 28 mm or less (see Non-Patent Document 1). . On the other hand, Al-Mg-based 5151 alloy (Al-1.5 to 2.1% Mg alloy) is used for a wide-mouth cap having a diameter of 38 mm or the like because it needs to have higher strength. However, a plate with higher strength and better openability is expected for contents that require a higher internal pressure or for gauge down (reduction in plate thickness).
このような高強度で開栓性の良いという期待に応えうる合金として、Al−Mg−Mn系合金がある。Al−Mg−Mn系合金板の最終冷間圧延率と結晶粒径を限定した先行技術(特許文献2参照)では、200MPa以上の引張強さとして263MPaの実施例があるが、その場合の伸びは2%であり、広口ボトル缶用のPPキャップとしては成形時に割れ等の不具合を発生するおそれがある。 As an alloy that can meet the expectation of such high strength and good openability, there is an Al-Mg-Mn alloy. In the prior art (refer to Patent Document 2) in which the final cold rolling rate and the crystal grain size of the Al—Mg—Mn alloy plate are limited, there is an example of 263 MPa as a tensile strength of 200 MPa or more. Is 2%, and PP caps for wide-mouth bottle cans may cause problems such as cracking during molding.
また、Al−Mg−Mn系合金の均質化処理から仕上げ焼鈍までの条件を限定した先行技術(特許文献3参照)では、引張強さは最大でも実施例で141MPa、比較例で152MPaであり、強度が低すぎて広口ボトル缶用PPキャップには適用できない。
さらにまた、急速加熱冷却による最終焼鈍条件を限定した先行技術(特許文献4参照)においても、引張強さの最大が185MPaであり、強度が低すぎる。
Moreover, in the prior art (refer patent document 3) which limited the conditions from the homogenization process of Al-Mg-Mn type alloy to finish annealing (refer patent document 3), the tensile strength is 141 MPa in an example at the maximum, and 152 MPa in a comparative example, The strength is too low to apply to PP caps for wide-bottle cans.
Furthermore, even in the prior art (see Patent Document 4) in which the final annealing conditions by rapid heating and cooling are limited (see Patent Document 4), the maximum tensile strength is 185 MPa, and the strength is too low.
一方、引張強さの高いAl−Mg−Mn系合金の例として、200MPaを超える実施例を示している先行技術(特許文献5参照)があるが、深絞りによるPPキャップ用ではなく、リングプルによる引き裂きで開栓する浅絞り広口キャップ用であり、スコア加工部の引き裂き性を重視したものであり、本発明とは用途が異なる。 On the other hand, as an example of an Al-Mg-Mn alloy having high tensile strength, there is a prior art (see Patent Document 5) showing an example exceeding 200 MPa, but it is not for a PP cap by deep drawing but by a ring pull. It is for shallow-drawn wide-mouthed caps that are opened by tearing, and emphasizes the tearability of the score processing part, and is used differently from the present invention.
本発明はかかる従来の問題点に鑑みてなされたもので、絞りカップの耳率が低く、かつ成形性を損なわない範囲で高強度化することにより、製造したキャップにおけるネジ部の剛性向上と天面のドーミング防止が可能となるように耐圧強度を向上することができる、Al−Mg−Mn系の広口ボトル缶キャップ用高強度アルミニウム合金板を提供する。 The present invention has been made in view of such conventional problems. By increasing the strength of the squeezed cup within a range where the ear ratio is low and the moldability is not impaired, the rigidity of the threaded portion of the manufactured cap can be improved. Provided is a high-strength aluminum alloy plate for Al-Mg-Mn-based wide-mouth bottle can caps, which can improve the pressure resistance so that surface doming can be prevented.
本発明は、塗装・印刷後に、直径28mmを超える円筒状のカップに成形し、該カップの耳部をトリミングした後、裾部にミシン目を加工し、その後、内容物が充填された飲料容器のネジ部に巻き締めされる広口ボトル缶キャップ用のアルミニウム合金板であって、
Mg:0.8%(重量%、以下同じ)超え、2.5%未満、および、Mn:0.3%以上、0.8%未満を含み、さらにCu:0.01〜0.24%、Cr:0.01〜0.05%、Zn:0.01〜0.25%、Si:0.01〜0.30%、Fe:0.01〜0.50%、Ti:0.005〜0.05%のうち1種または2種以上を含み、残部が不可避的不純物とアルミニウムからなる化学組成を有し、
該アルミニウム合金板の元板の引張強さが200〜300MPa、耐力が150〜250MPaであり、
かつ、上記元板に対して、200℃の温度で10分間保持する熱処理を施した空焼板の引張強さが200〜300MPa、耐力が140〜240MPa、伸びが5%以上であることを特徴とする広口ボトル缶キャップ用高強度アルミニウム合金板にある(請求項1)。
The present invention, after painting / printing, is formed into a cylindrical cup having a diameter of more than 28 mm, trims the ear of the cup, then processes the perforation at the hem, and then the beverage container filled with the contents An aluminum alloy plate for a wide-mouth bottle can cap that is wound around the screw part of
Mg: more than 0.8% (weight%, the same applies hereinafter), less than 2.5%, and Mn: not less than 0.3% and less than 0.8%, and further Cu: 0.01 to 0.24% Cr: 0.01-0.05%, Zn: 0.01-0.25%, Si: 0.01-0.30%, Fe: 0.01-0.50%, Ti: 0.005 It contains one or more of 0.05%, and the balance has a chemical composition consisting of inevitable impurities and aluminum ,
The tensile strength of the base plate of the aluminum alloy plate is 200 to 300 MPa, the proof stress is 150 to 250 MPa,
And the tensile strength of the blank board which gave the heat processing hold | maintained for 10 minutes at the temperature of 200 degreeC with respect to the said base plate is 200-300 MPa, yield strength is 140-240 MPa, elongation is 5% or more, It is characterized by the above-mentioned. It is in the high intensity | strength aluminum alloy plate for wide-mouth bottle can caps made into (1).
まず、本発明における化学組成の限定理由について説明する。
Mgは、本発明の必須の成分であり、その含有量を0.8%超え、2.5%未満に限定することにより、強度および成形性を良好に保つことができる。
Mg含有量が0.8%以下の場合、高内圧の内容物対応あるいはゲージダウン対応には強度不足になるため、広口ボトル缶キャップ(以下、適宜、単にキャップという。)として所定の耐圧を得ることができない。また、成形したキャップにおけるネジ部の剛性向上と天面のドーミング防止効果が十分に得られないという問題もある。また、圧延方向に対し0°、90°、180°および270°方向の4箇所の耳が発達しやすくなるため、安定して低い耳率の材料を得ることが難しく、文字曲がりのしにくいキャップを量産していくことは容易ではない。ここで言う文字曲がりとは、平板状態で印刷を施した後にカップ状に成形するキャップの製造方法の特性上、素材の変形の仕方によって、印刷した絵柄や文字等が曲がって表示される現象のことをいう。
Mg含有量が多いほど結晶粒が細かくなるので、Mg含有量を高めて結晶粒微細化効果を高めることで、カップ成形時の肌荒れも抑制しやすくなる。
First, the reason for limiting the chemical composition in the present invention will be described.
Mg is an essential component of the present invention. By limiting the content to more than 0.8% and less than 2.5%, the strength and formability can be kept good.
When the Mg content is 0.8% or less, the strength is insufficient to cope with high internal pressure contents or gauge down, so that a predetermined pressure resistance is obtained as a wide-mouth bottle can cap (hereinafter simply referred to as a cap). I can't. In addition, there is a problem that the rigidity of the threaded portion in the molded cap and the effect of preventing doming on the top surface cannot be sufficiently obtained. In addition, four ears in the 0 °, 90 °, 180 °, and 270 ° directions with respect to the rolling direction are easily developed, so it is difficult to stably obtain a material with a low ear rate, and it is difficult to bend characters. It is not easy to mass-produce. Character bending referred to here is a phenomenon in which printed pictures and characters are bent and displayed depending on how the material is deformed due to the characteristics of the method of manufacturing a cap that is molded into a cup shape after printing in a flat state. That means.
The larger the Mg content, the finer the crystal grains. By increasing the Mg content and enhancing the crystal grain refining effect, it becomes easy to suppress rough skin during cup molding.
一方、Mg含有量が2.5%以上の場合、強度が高すぎて、開栓時に多大な力を要するため、開栓しにくくなってしまう。そのため、Mg含有量は2.5%未満が好ましい。なお、Mg含有量は、上述の異方性と強度をバランスよく満足し製造しやすくするために、より好ましくは1.3%超え、2.2%未満、さらに好ましくは1.5%超え、2.0%未満がよい。 On the other hand, when the Mg content is 2.5% or more, the strength is too high, and a great deal of force is required at the time of opening, which makes it difficult to open. Therefore, the Mg content is preferably less than 2.5%. The Mg content is preferably more than 1.3%, less than 2.2%, more preferably more than 1.5%, in order to satisfy the above-described anisotropy and strength in a balanced manner and facilitate production. Less than 2.0% is good.
Mnは、強度と成形性を良好に保つために、本発明の必須の成分である。また、Mnを必須成分とすることによって、その原料として、例えば缶ボディ材3004合金、3104合金をリサイクルして使いやすくなる。Mn含有量は0.3%以上、1.5%以下に限定する。Mn含有量が0.3%未満の場合、強度不足でキャップとして所定の性能を得にくく、またリサイクル材を多く使用しにくい。また、1.5%超えの場合、強度が高すぎて開栓時に多大な力を要し開栓しにくくなったり、Feなどの元素とともに鋳造時に巨大な金属間化合物を作りやすい。
Mn含有量は、好ましくは0.3%以上、0.8%未満とする。このようなMn量の上限抑制の理由は、Mg含有量が多いほど成形性維持のまま高強度化できるが、鋳塊を高温で均質化処理できず、耳率に影響するMn系析出物の制御がしにくくなるからである。
Mn is an essential component of the present invention in order to maintain good strength and moldability. In addition, by using Mn as an essential component, for example, can body material 3004 alloy and 3104 alloy can be recycled and used as the raw material. The Mn content is limited to 0.3% or more and 1.5% or less. When the Mn content is less than 0.3%, it is difficult to obtain a predetermined performance as a cap due to insufficient strength, and it is difficult to use a lot of recycled materials. On the other hand, if it exceeds 1.5%, the strength is so high that a large amount of force is required at the time of opening and it is difficult to open, or a huge intermetallic compound is easily produced at the time of casting together with elements such as Fe.
The Mn content is preferably 0.3% or more and less than 0.8%. The reason for suppressing the upper limit of the amount of Mn is that the higher the Mg content, the higher the strength while maintaining the formability, but the ingot cannot be homogenized at high temperature, and the Mn-based precipitates that affect the ear rate are affected. This is because it becomes difficult to control.
耳率の発生状態及び強度特性は、Mg、Mnの含有量だけではなく、その他の製造条件などによっても調整できる。 The generation state and strength characteristics of the ear rate can be adjusted not only by the contents of Mg and Mn but also by other manufacturing conditions.
なお、上記元板とは、本発明のアルミニウム合金板そのもの、すなわち製造したままの状態であり、キャップ製造工程に供給される前の状態の板をいう。そして、上記空焼板とは、この元板に、上記の熱処理を施して、便宜上キャップ製造工程における印刷後の状態をある程度反映させた状態の板をいう。 The above-mentioned base plate refers to the aluminum alloy plate of the present invention itself, that is, the state as manufactured and the state before being supplied to the cap manufacturing process. The blank plate is a plate in which the base plate is subjected to the heat treatment as described above, and the state after printing in the cap manufacturing process is reflected to some extent for convenience.
上記元板の強度は、引張強さが200〜300MPa、耐力が150〜250MPaの範囲に限定する。そして、かつ、上記空焼板の強度は、引張強さが200〜300MPa、耐力が140〜240MPa、伸びが5%以上の範囲に限定する。
上記元板の引張強さ及び耐力が上記範囲にないと、空焼後に目的とする強度を得ることが困難となる。
上記空焼板の引張強さが200MPa未満の場合及び耐力が140MPa未満の場合には、成形したキャップにおいて所定の耐圧を得ることができない。一方、空焼板の引張強さが300MPaを超える場合及び耐力が240MPaを超える場合には、成形したキャップの開栓がしにくくなるという問題がある。上記空焼板の伸びが5%未満の場合には、キャップ成形時に割れなどの成形不良が出やすくなるという問題がある。
The strength of the base plate is limited to a tensile strength of 200 to 300 MPa and a proof stress of 150 to 250 MPa. And the intensity | strength of the said baked board is limited to the range whose tensile strength is 200-300 MPa, proof stress is 140-240 MPa, and elongation is 5% or more.
If the tensile strength and proof stress of the base plate are not within the above ranges, it will be difficult to obtain the desired strength after baking.
When the tensile strength of the blank plate is less than 200 MPa and the proof stress is less than 140 MPa, a predetermined pressure resistance cannot be obtained in the molded cap. On the other hand, when the tensile strength of the blank plate exceeds 300 MPa and when the proof stress exceeds 240 MPa, there is a problem that it is difficult to open the molded cap. When the elongation of the blank plate is less than 5%, there is a problem that molding defects such as cracks are likely to occur during cap molding.
本発明においては、得ようとするキャップの仕様に応じて、Mg含有量をより狭い範囲に限定して、より最適な強度特性に調整することができる。
すなわち、キャップの開栓しやすさを重視する場合には、Mg含有量は1.3%超え、2.2%未満であり、かつ、上記元板の引張強さが210〜280MPa、耐力が160〜250MPaであると共に、上記空焼板の引張強さが210〜280MPa、耐力が150〜240MPa、伸びが5%以上であることが好ましい(請求項2)。
In the present invention, according to the specifications of the cap to be obtained, the Mg content can be limited to a narrower range and adjusted to a more optimal strength characteristic.
That is, when emphasizing the ease of opening the cap, the Mg content is more than 1.3% and less than 2.2%, the tensile strength of the base plate is 210 to 280 MPa, and the proof stress is In addition to 160 to 250 MPa, it is preferable that the blank plate has a tensile strength of 210 to 280 MPa, a proof stress of 150 to 240 MPa, and an elongation of 5% or more.
また、上記アルミニウム合金板の化学組成は、さらにCu:0.01〜0.24%、Cr:0.01〜0.05%、Zn:0.01〜0.25%、Si:0.01〜0.30%、Fe:0.01〜0.50%、Ti:0.005〜0.05%のうち1種または2種以上を含む。 Moreover, the chemical composition of the said aluminum alloy plate is further Cu: 0.01-0.24%, Cr: 0.01-0.05%, Zn: 0.01-0.25%, Si: 0.01 One type or two or more types are included among -0.30%, Fe: 0.01-0.50%, and Ti: 0.005-0.05% .
Cu:0.01〜0.24%;
Cuは、材料強度に影響を及ぼす元素である。0.01%未満の場合、その効果が得られないばかりでなく、純度の高い地金を使用する必要があり、コストアップとなる。0.24%を超えての添加は、圧延加工しにくくなる。
Cu: 0.01 to 0.24%;
Cu is an element that affects the material strength. If it is less than 0.01%, not only the effect cannot be obtained, but it is necessary to use a high purity metal, resulting in an increase in cost. Addition exceeding 0.24% makes rolling difficult.
Cr:0.01〜0.05%、Zn:0.01〜0.25%、Fe:0.01〜0.50%;
Cr、Zn、Feは、結晶粒微細化による成形性に影響を及ぼす元素である。それぞれ上記下限未満の場合、その効果が得られないばかりでなく、純度の高い地金を使用する必要があり、コストアップとなる。一方、上記上限を超える場合、結晶粒微細化効果は飽和するため、添加に要するコストアップを考慮すると上記上限とすることが好ましい。
Cr: 0.01-0.05%, Zn: 0.01-0.25%, Fe: 0.01-0.50%;
Cr, Zn, and Fe are elements that affect the formability by crystal grain refinement. If each of these is less than the above lower limit, not only the effect cannot be obtained, but it is necessary to use a high purity metal, resulting in an increase in cost. On the other hand, when the above upper limit is exceeded, the crystal grain refining effect is saturated. Therefore, the upper limit is preferably taken into consideration in view of the cost increase required for addition.
Si:0.01〜0.30%;
Siは、MnやFeと化合物を形成し、鋳造時にAl−Mn−Fe−Si系やAl−Fe−Si系化合物等の晶出物を形成する元素である。0.01%未満の場合、純度の高い地金を使用する必要があり、コストアップとなる。0.30%を超える場合、前記晶出物が多くなり、キャップ成形性を劣化させる。
Si: 0.01-0.30%;
Si is an element that forms a compound with Mn and Fe and forms a crystallized product such as an Al-Mn-Fe-Si-based or Al-Fe-Si-based compound during casting. If it is less than 0.01%, it is necessary to use high purity metal, which increases costs. When it exceeds 0.30%, the crystallized matter increases and the cap moldability is deteriorated.
Ti:0.005〜0.05%;
Tiは、鋳塊組織微細化による成形性向上に影響を及ぼす元素である。0.005%未満の場合、その効果が得られない。0.05%を超えると、未固溶のAl−Ti系化合物が最終製品の表面欠陥として現れやすくなる。
なお、鋳塊組織微細化剤としてAl−Ti−B中間合金を添加する場合は、Bが含有されるが、Bは0.02%以下の範囲で添加されるのが好ましい。
Ti: 0.005 to 0.05%;
Ti is an element that affects the improvement of formability by refining the ingot structure. If it is less than 0.005%, the effect cannot be obtained. If it exceeds 0.05%, an insoluble Al—Ti compound tends to appear as a surface defect in the final product.
In addition, when adding an Al-Ti-B intermediate alloy as an ingot structure | tissue refiner, B contains, but it is preferable to add B in 0.02% or less of range.
次に、上記アルミニウム合金板は、上記元板又は上記空焼板の耳率試験に使用する絞りカップの開口部に発生する耳のうち、圧延方向に対し45°方向の4箇所(45°、135°、225°、315°方向の4箇所)、及び0°、90°、180°、270°方向の4箇所に発生する耳の耳率が2.5%以下であり、かつ圧延方向に対し0°と180°方向の2箇所に発生する耳の耳率が2.0%以下であることが好ましい(請求項3)。 Next, the aluminum alloy plate has four locations (45 °, 45 ° in the rolling direction) with respect to the rolling direction among the ears generated in the opening portion of the drawn cup used for the ear rate test of the base plate or the blank plate. 135 °, 225 °, four points of 315 ° direction), and 0 °, 90 °, 180 ° , and the ear ear rate occurring at four positions 270 ° direction of 2.5% or less, and the rolling direction it is preferable 0 ° and ears ears rates occurring in two places in the 180 ° direction against the 2.0% or less (claim 3).
上記45°方向4箇所の耳の耳率が2.5%を超えた場合、成形したキャップの裾部の印刷文字等の曲がりは45°方向において顕著となり、防止が困難となる。耳率は小さければ小さい程、つまり下限は0%であるのがよいが、金属板の性質上困難である。実際のところ0.5%〜2.0%の耳率であればより好ましい。 When the ear rate of the four ears in the 45 ° direction exceeds 2.5%, bending of printed characters or the like at the skirt portion of the molded cap becomes noticeable in the 45 ° direction and is difficult to prevent. The smaller the ear ratio, that is, the lower limit is preferably 0%, but it is difficult due to the nature of the metal plate. Actually, an ear rate of 0.5% to 2.0% is more preferable.
また、0°、90°、180°、270°方向の4箇所に発生する耳の耳率が2.0%を超えた場合においても、上記45°方向4箇所における耳率が2.0%を超えた場合と同様に、印刷文字等の曲がりが顕著になる。 Further, even when the ear rate of the ears occurring at the four locations in the 0 °, 90 °, 180 °, and 270 ° directions exceeds 2.0%, the ear rate at the four locations in the 45 ° direction is 2.0%. As in the case of exceeding, bending of printed characters or the like becomes remarkable.
さらに、圧延方向に対し0°と180°方向の2箇所に発生する耳の耳率が2.0%を超えた場合にも、成形したキャップ裾部の印刷文字等の曲がりを防止することが困難となる。Al−低Mg系合金の絞り加工の場合、圧延方向に対し特に0°と180°方向の耳が発生しやすく、この方向の耳を制御することがポイントとなる。そして、より確実に印刷文字等の曲がりを抑制するには、圧延方向に対し0°と180°に発生する耳の耳率を1.5%以下とすることが好ましい。 Furthermore, even when the ear-ear ratio occurring at two locations in the 0 ° and 180 ° directions with respect to the rolling direction exceeds 2.0%, it is possible to prevent bending of printed characters and the like on the molded cap hem portion. It becomes difficult. In the case of drawing of an Al-low Mg alloy, ears in the directions of 0 ° and 180 ° are particularly likely to occur with respect to the rolling direction, and it is important to control the ears in this direction. And in order to suppress the bending of printed characters and the like more reliably, it is preferable to set the ear ratio of the ears generated at 0 ° and 180 ° with respect to the rolling direction to 1.5% or less.
ここで、上記絞りカップは、上記キャップ用Al−Mg系合金板より切り出したブランクを所定の条件で絞り加工して得られるカップ状の試験材である。この絞りカップの開口端において、軸方向に突出した部分を耳、耳と耳との間において最も窪んだ部分を谷という。そして、絞りカップの底から耳先端までの距離を耳高さとし、絞りカップの底から谷先端までを谷高さとする。そして耳率は、次のようにして算出することができる。 Here, the drawn cup is a cup-shaped test material obtained by drawing a blank cut out from the cap Al—Mg alloy plate under predetermined conditions. At the opening end of the throttle cup, the portion protruding in the axial direction is called an ear, and the most depressed portion between the ears is called a valley. The distance from the bottom of the squeeze cup to the tip of the ear is defined as the ear height, and the distance from the bottom of the squeeze cup to the tip of the valley is defined as the valley height. The ear rate can be calculated as follows.
<45°方向4箇所の耳の耳率>
45°耳高さ=A、135°耳高さ=B、225°耳高さ=C、315°耳高さ=D、
45°と135°の間の最小の谷高さ=E、
135°と225°の間の最小の谷高さ=F、
225°と315°の間の最小の谷高さ=G、
315°と45°の間の最小の谷高さ=H、
耳部の平均:M45=(A+B+C+D)/4、
谷部の平均:V45=(E+F+G+H)/4とすると、
耳率=〔(M45−V45)/{(M45+V45)/2}〕×100(%)
<Ear rate of ears at 45 points in 45 ° direction>
45 ° ear height = A, 135 ° ear height = B, 225 ° ear height = C, 315 ° ear height = D,
Minimum valley height between 45 ° and 135 ° = E,
Minimum valley height between 135 ° and 225 ° = F,
Minimum valley height between 225 ° and 315 ° = G,
Minimum valley height between 315 ° and 45 ° = H,
Ear average: M45 = (A + B + C + D) / 4,
Average valley: V45 = (E + F + G + H) / 4
Ear rate = [(M45−V45) / {(M45 + V45) / 2}] × 100 (%)
<0°、90°、180°、270°方向4箇所の耳の耳率>
0°耳高さ=A’、90°耳高さ=B’、180°耳高さ=C’、270°耳高さ=D’、0°と90°の間の最小の谷高さ=E’、
90°と180°の間の最小の谷高さ=F’、
180°と270°の間の最小の谷高さ=G’、
270°と0°の間の最小の谷高さ=H’、
耳部の平均:M’=(A’+B’+C’+D’)/4、
谷部の平均:V’=(E’+F’+G’+H’)/4とすると、
耳率=〔(M’−V’)/{(M’+V’)/2}〕×100(%)
<Ear rate of ears at 4 locations in 0 °, 90 °, 180 °, 270 ° direction>
0 ° ear height = A ′, 90 ° ear height = B ′, 180 ° ear height = C ′, 270 ° ear height = D ′, minimum valley height between 0 ° and 90 ° = E ',
Minimum valley height between 90 ° and 180 ° = F ′,
Minimum valley height between 180 ° and 270 ° = G ′,
Minimum valley height between 270 ° and 0 ° = H ′,
Ear average: M ′ = (A ′ + B ′ + C ′ + D ′) / 4
Average valley: V ′ = (E ′ + F ′ + G ′ + H ′) / 4
Ear rate = [(M′−V ′) / {(M ′ + V ′) / 2}] × 100 (%)
<0°と180°方向2箇所の耳の耳率>
カップの平均高さ=P(開口端の高さを1000点測定した平均高さ)、
0°耳高さ=Q、180°耳高さ=R、
耳部の平均:S=(Q+R)/2、
耳率={(S−P)/P}×100(%)
<Ear ratio of ears at two locations at 0 ° and 180 °>
Average height of cup = P (average height obtained by measuring the height of the open end at 1000 points),
0 ° ear height = Q, 180 ° ear height = R,
Ear average: S = (Q + R) / 2,
Ear rate = {(SP) / P} × 100 (%)
<カップ絞り成形条件>
ダイス径33.6mm、ポンチ径33mm、ポンチ肩R1.5mmの金型を用い、供試材ブランク径55mmとして、絞り比1.67でカップ絞りを実施。
<Cup drawing molding conditions>
Using a die with a die diameter of 33.6 mm, a punch diameter of 33 mm, and a punch shoulder R of 1.5 mm, a cup blank was carried out with a drawing material blank diameter of 55 mm and a drawing ratio of 1.67.
また、上記アルミニウム合金板は、その板厚が0.20〜0.26mmであることが好ましい(請求項4)。
すなわち、広口ボトル缶キャップ用アルミニウム合金板の板厚は、本発明の課題であるキャップの耐圧に影響を与える。板厚が厚いほど耐圧強度は大きくなるが、省資源の点からは板厚は薄い方が好ましい。本発明では、上記のごとく高強度化を図ることによって、所定の耐圧強度を保ちながら板厚を薄くすることが可能となる。従来は、0.25mm未満の板厚は耐圧の点から困難であったが、本発明では、0.20mm以上、0.25mm未満の板厚を適用しても十分な耐圧を得ることが可能である。さらに、0.25〜0.26mmの場合は、高耐圧の要求に対してより高強度化を図ることが可能となる。板厚が0.20mm未満の場合には、現行のキャップ形状では所定の耐圧強度が得られないが、技術の進歩によってキャップ形状が改良された場合は、本発明材で実用化が可能となると考えられる。
Further, the aluminum alloy plate preferably has a thickness is 0.20~0.26Mm (claim 4).
That is, the thickness of the aluminum alloy plate for the wide-mouth bottle can cap affects the pressure resistance of the cap, which is the subject of the present invention. The thicker the plate, the greater the pressure resistance, but the thinner the plate is preferable from the viewpoint of resource saving. In the present invention, by increasing the strength as described above, it becomes possible to reduce the plate thickness while maintaining a predetermined pressure strength. Conventionally, a plate thickness of less than 0.25 mm has been difficult from the viewpoint of pressure resistance, but in the present invention, sufficient pressure resistance can be obtained even when a plate thickness of 0.20 mm or more and less than 0.25 mm is applied. It is. Further, in the case of 0.25 to 0.26 mm, it is possible to further increase the strength with respect to the demand for a high breakdown voltage. When the plate thickness is less than 0.20 mm, the current cap shape does not provide a predetermined pressure strength. However, when the cap shape is improved by technological advancement, the material of the present invention can be put to practical use. Conceivable.
次に、本発明のアルミニウム合金板を得るための好ましい製造条件について説明する。
基本的な製造工程は、鋳塊を均質化熱処理した後、熱間圧延をして板を形成し、焼鈍、冷間圧延、焼鈍、冷間圧延を順次行って製品板厚とし、最後に強度の安定化のために安定化熱処理することである。なお、この安定化熱処理の前あるいは後において、脱脂、化成処理等の表面処理をすることが多い。
Next, preferable production conditions for obtaining the aluminum alloy plate of the present invention will be described.
The basic manufacturing process is to homogenize and heat the ingot, then hot-roll to form a plate, and then anneal, cold-roll, anneal, and cold-roll sequentially to obtain the product thickness, and finally strength In order to stabilize the heat treatment, stabilization heat treatment is performed. In many cases, surface treatment such as degreasing and chemical conversion treatment is performed before or after the stabilization heat treatment.
上記均質化熱処理は、鋳塊を450〜550℃の温度に1〜24時間保持する条件である。保持温度450℃未満あるいは保持時間が1時間未満であると耳の生成が不安定となり制御が困難となる。保持温度が550℃超えあるいは保持時間が24時間超えの場合、表面にMgが拡散しやすく、表面の酸化Mg層が厚くなり、面削量を過度に多くする必要があり非経済的である。 The said homogenization heat processing is the conditions which hold | maintain an ingot at the temperature of 450-550 degreeC for 1 to 24 hours. If the holding temperature is less than 450 ° C. or the holding time is less than 1 hour, the ear formation becomes unstable and control becomes difficult. When the holding temperature exceeds 550 ° C. or the holding time exceeds 24 hours, Mg easily diffuses on the surface, the Mg oxide layer on the surface becomes thick, and the amount of chamfering needs to be excessively increased, which is uneconomical.
続いて、例えば、熱間圧延−焼鈍1−冷間圧延1−焼鈍2−冷間圧延2−安定化熱処理を順次行う。この工程で、所定の強度と耳率を得ることができる。
上記焼鈍1、2では、300〜550℃の温度に保持する条件で行う。保持温度が300℃未満の場合、最終板で所定の耳率が得られず、また、強度が高くなりすぎて成形性に劣る。保持温度が550℃超えの場合、表面が酸化しやすくなり好ましくない。なお、保持時間は特に限定しないが、連続焼鈍ラインなどによる急速加熱・急速冷却の比較的高温での焼鈍の場合、保持0〜20秒、バッチ式焼鈍炉による比較的低温での焼鈍の場合保持30分〜5時間が適当である。
Subsequently, for example, hot rolling, annealing, cold rolling, annealing, cold rolling, and stabilizing heat treatment are sequentially performed. In this step, a predetermined strength and ear rate can be obtained.
In the said annealing 1 and 2, it carries out on the conditions hold | maintained at the temperature of 300-550 degreeC. When the holding temperature is less than 300 ° C., a predetermined ear ratio cannot be obtained with the final plate, and the strength becomes too high and the moldability is poor. When the holding temperature exceeds 550 ° C., the surface tends to be oxidized, which is not preferable. The holding time is not particularly limited, but when annealing at a relatively high temperature such as rapid heating / cooling using a continuous annealing line or the like, holding is performed for 0 to 20 seconds, holding when annealing at a relatively low temperature using a batch annealing furnace. 30 minutes to 5 hours is appropriate.
上記焼鈍2後の冷間圧延2は、30〜70%の範囲で行えばよい。圧延率が30%未満では所定の強度を得にくく、所定の耳率を得にくくなる。圧延率が70%超えでは、成形性が低下し強度が高すぎて開栓しにくくなり、また、圧延集合組織が発達しすぎて45°方向の耳が大きくなる。 What is necessary is just to perform the cold rolling 2 after the said annealing 2 in 30 to 70% of range. When the rolling rate is less than 30%, it is difficult to obtain a predetermined strength, and it becomes difficult to obtain a predetermined ear rate. If the rolling rate exceeds 70%, the formability is lowered, the strength is too high and it is difficult to open the plug, and the rolling texture is developed so much that the ears in the 45 ° direction become large.
キャップ用素材としての性能は冷間圧延のままでほぼ達成されるが、Al−Mg系合金の場合、冷間圧延のままの状態で室温放置すると、強度が次第に低下する現象が起こる。それを防止し強度を安定化させるために、100〜300℃の温度で30分以上加熱する熱処理(安定化熱処理)が必要である。100℃未満では強度が安定せず、上限の300℃を超えると、軟化が大きくなり所定の強度を得ることができない。 The performance as a cap material is almost achieved with cold rolling, but in the case of an Al-Mg alloy, when the cold rolling is left at room temperature, a phenomenon in which the strength gradually decreases occurs. In order to prevent this and stabilize the strength, a heat treatment (stabilized heat treatment) for heating at a temperature of 100 to 300 ° C. for 30 minutes or more is necessary. If it is less than 100 ° C., the strength is not stable, and if it exceeds the upper limit of 300 ° C., softening increases and a predetermined strength cannot be obtained.
本発明の内容を具体的な実施例により説明するが、以下は本発明の一実施態様を示したものであり、本発明はこれに限定されるものではない。
(実施例1)
表1に示す化学成分を含有するアルミニウム合金鋳塊を半連続鋳造にて造塊し、表面の偏析層を切削後、500℃で6時間保持する均質化熱処理し、均質化熱処理炉から出してすぐに熱間圧延を開始した。熱間圧延は、板厚3mmで終了し、焼鈍を行うことで再結晶組織を得た後に、所定の板厚まで冷間圧延し、さらに中間焼鈍して再結晶組織とした後、50%の冷間加工度で、製品板厚まで冷間圧延し、安定化熱処理して供試材とした。
The contents of the present invention will be described with reference to specific examples, but the following shows one embodiment of the present invention and the present invention is not limited thereto.
Example 1
Aluminum alloy ingots containing the chemical components shown in Table 1 are ingoted by semi-continuous casting, and after the segregation layer on the surface is cut, homogenized heat treatment is maintained at 500 ° C. for 6 hours, and then removed from the homogenized heat treatment furnace. Hot rolling was started immediately. Hot rolling is finished at a sheet thickness of 3 mm, and after recrystallization is obtained by annealing, cold rolling is performed to a predetermined sheet thickness, and further intermediate annealing is performed to obtain a recrystallized structure. The specimens were cold-rolled to the product thickness at the cold working degree and subjected to stabilization heat treatment.
得られた7種類の供試材E1〜E7を用い、以下の評価試験をした。一部の試験片は、材料組織観察をした。
<機械的性質>
JIS5号試験片にて、引張試験した。
The following evaluation tests were performed using the obtained seven types of test materials E1 to E7. Some specimens were observed for material structure.
<Mechanical properties>
A tensile test was performed using a JIS No. 5 test piece.
<耳率>
ダイス径33.6mm、ポンチ径33mm、ポンチ肩R1.5mmの金型を用い、供試材ブランク径55mmとして、絞り比1.67でカップ絞りを実施。
耳率は、前述の条件により成形したカップを、前述の式から、45°方向4箇所(A方向)の耳の耳率、あるいは0°、90°、180°、270°方向4箇所(B方向)の耳の耳率、及び0°と180°方向2箇所の耳の耳率を測定した。
<Ear rate>
Using a die with a die diameter of 33.6 mm, a punch diameter of 33 mm, and a punch shoulder R of 1.5 mm, a cup blank was carried out with a drawing material blank diameter of 55 mm and a drawing ratio of 1.67.
The ear rate is calculated based on the above-mentioned conditions, and the ear rate of ears at 45 locations in the 45 ° direction (A direction) or 4 locations at 0 °, 90 °, 180 °, and 270 ° directions (B The ear rate of the ears in the direction) and the ear rates of the ears at two locations in the 0 ° and 180 ° directions were measured.
<結晶粒径>
供試材板面を電解研磨し、偏光顕微鏡で結晶粒を観察した。ASTMカードを用いて、比較法から、結晶粒径を求めた。
<Crystal grain size>
The plate surface of the test material was electropolished and the crystal grains were observed with a polarizing microscope. The crystal grain size was determined from the comparative method using an ASTM card.
<文字曲がり>
文字曲がりは、キャップ開口端部から3〜5mmの位置に文字が来るように、絞り前のブランクに10文字の印刷をし、直径38mmより絞り比が厳しい直径28mmPPキャップ用カップを絞り成形し、文字曲がりを目視観察して評価した。
<キャップ成形性>
成形後のキャップ用のカップの外観において、割れ、しわ、肌荒れ等の欠陥の有無を目視確認した。
<Character bending>
10 characters are printed on the blank before drawing so that the character comes to a position 3 to 5 mm from the cap opening end, and a 28 mm diameter PP cap cup with a stricter drawing ratio than 38 mm is drawn, Character bending was visually observed and evaluated.
<Cap formability>
The appearance of the cap cup after molding was visually confirmed for the presence of defects such as cracks, wrinkles, and rough skin.
表2にこれらの評価結果を示す。本例の供試材E1〜E7は、機械的性質、耳率、結晶粒径、文字曲がり、キャップ成形性というすべての評価項目において、いずれも広口ボトル缶キャップ用のキャップ材として良好な結果を示した。 Table 2 shows the evaluation results. The test materials E1 to E7 of this example have good results as cap materials for wide-mouth bottle can caps in all the evaluation items of mechanical properties, ear ratio, crystal grain size, letter bending, and cap moldability. Indicated.
(比較例1)
表3に示すMgの含有量が本発明の請求範囲外である成分を有するアルミニウム合金鋳塊を、前述の実施例1と同じ条件で製造し、供試材C1、C2を得た。
(Comparative Example 1)
An aluminum alloy ingot having a component whose Mg content shown in Table 3 is outside the scope of the present invention was manufactured under the same conditions as in Example 1 to obtain specimens C1 and C2.
これらの評価結果を表4に示す。
表4から知られるように、供試材C1は、Mg量及びMn量が本発明の下限未満であるので、高強度を得ることができず、高耐圧のかかる製品には適さない。
供試材C2は、Mg量が本発明の上限を超えるため、強度が高すぎ、開栓しにくいキャップとなり、適さない。
These evaluation results are shown in Table 4.
As can be seen from Table 4, the sample material C1 has an Mg amount and an Mn amount that are less than the lower limit of the present invention, so that high strength cannot be obtained, and it is not suitable for a product with high pressure resistance.
Since the amount of Mg exceeds the upper limit of the present invention, the sample material C2 is not suitable because the strength is too high and the cap is difficult to open.
Claims (4)
Mg:0.8%(重量%、以下同じ)超え、2.5%未満、および、Mn:0.3%以上、0.8%未満を含み、さらにCu:0.01〜0.24%、Cr:0.01〜0.05%、Zn:0.01〜0.25%、Si:0.01〜0.30%、Fe:0.01〜0.50%、Ti:0.005〜0.05%のうち1種または2種以上を含み、残部が不可避的不純物とアルミニウムからなる化学組成を有し、
該アルミニウム合金板の元板の引張強さが200〜300MPa、耐力が150〜250MPaであり、
かつ、上記元板に対して、200℃の温度で10分間保持する熱処理を施した空焼板の引張強さが200〜300MPa、耐力が140〜240MPa、伸びが5%以上であることを特徴とする広口ボトル缶キャップ用高強度アルミニウム合金板。 After painting and printing, the cup is molded into a cylindrical cup with a diameter of more than 28 mm, the ears of the cup are trimmed, the perforations are processed in the hem, and then the beverage container filled with contents is threaded An aluminum alloy plate for a wide-mouth bottle can cap to be wound,
Mg: more than 0.8% (weight%, the same applies hereinafter), less than 2.5%, and Mn: not less than 0.3% and less than 0.8%, and further Cu: 0.01 to 0.24% Cr: 0.01-0.05%, Zn: 0.01-0.25%, Si: 0.01-0.30%, Fe: 0.01-0.50%, Ti: 0.005 It contains one or more of ~ 0.05%, the balance has a chemical composition consisting of inevitable impurities and aluminum ,
The tensile strength of the base plate of the aluminum alloy plate is 200 to 300 MPa, the proof stress is 150 to 250 MPa,
And the tensile strength of the blank board which gave the heat processing hold | maintained for 10 minutes at the temperature of 200 degreeC with respect to the said base plate is 200-300 MPa, yield strength is 140-240 MPa, elongation is 5% or more, It is characterized by the above-mentioned. High-strength aluminum alloy plate for wide-mouth bottle can caps.
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