JP2000001730A - Aluminum alloy sheet for can body, and its production - Google Patents
Aluminum alloy sheet for can body, and its productionInfo
- Publication number
- JP2000001730A JP2000001730A JP16974098A JP16974098A JP2000001730A JP 2000001730 A JP2000001730 A JP 2000001730A JP 16974098 A JP16974098 A JP 16974098A JP 16974098 A JP16974098 A JP 16974098A JP 2000001730 A JP2000001730 A JP 2000001730A
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- alloy sheet
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Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、高強度で、耳が低
く、耐孔食性、しごき成形性などに優れ、2ピースDI
缶の薄肉軽量化を実現できる缶胴用Al合金板およびそ
の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a two-piece DI having high strength, low ears, excellent pitting resistance and ironing formability.
The present invention relates to an aluminum alloy plate for a can body capable of realizing a thin and lightweight can and a method for producing the same.
【0002】[0002]
【従来の技術】缶胴用Al合金板には、製缶に要求され
る、絞り、しごき、フランジ(蓋巻締め部)の各成形性
に優れるJIS3004合金 (Si0.3,Fe0.7,Cu0.25,Mn
1.0〜1.5, Mg0.8〜1.3,Zn0.25wt%)、JIS3104合
金などが用いられている。そして、前記缶胴用Al合金
板は、例えば、JIS3004合金鋳塊に均質化処理、
熱間圧延、焼鈍処理、冷間圧延を施して製造されている
(特開昭61−288055号公報参照)。ところで、近年、D
I缶の薄肉軽量化が強く求められる中で、缶胴用Al合
金板には高強度で成形性に優れる材料が要求され、例え
ば、JIS3004合金を改良した材料(特開昭61−28
8055号公報)などが提案されている。しかし、いずれの
材料にも、強度を高めるとしごき成形時に焼付きが生
じ、また孔食も起き易くなるといった問題がある。2. Description of the Related Art JIS 3004 alloys (Si0.3, Fe0.7, Cu0) which are excellent in formability of drawing, ironing, and flange (lid-tightened portion) required for can-making are used for Al alloy sheets for can bodies. .25, Mn
1.0-1.5, Mg 0.8-1.3, Zn 0.25 wt%), JIS 3104 alloy and the like are used. The aluminum alloy plate for the can body is, for example, homogenized into a JIS 3004 alloy ingot,
It is manufactured by subjecting it to hot rolling, annealing, and cold rolling (see JP-A-61-288055). By the way, in recent years, D
With the strong demand for thinner and lighter I-cans, Al alloy sheets for can bodies are required to have high strength and excellent formability. For example, a material obtained by improving JIS 3004 alloy (Japanese Patent Laid-Open No. 61-28)
No. 8055) has been proposed. However, any of these materials has a problem in that, when the strength is increased, seizure occurs during ironing and pitting tends to occur.
【0003】[0003]
【発明が解決しようとする課題】このようなことから、
本発明者等は、缶胴用Al合金について種々検討を行っ
たところ、JIS3004合金中のSi量を増加させる
ことにより、強度およびしごき成形性が改善されるこ
と、またZnを増加させることにより孔食も低減できる
ことを見いだした。しかし、しごき成形時などで耳(缶
の先端のギザギザ)が高くなり、この耳はトリミングす
るため、製造歩留まりが低下するという新たな問題が生
じた。SUMMARY OF THE INVENTION
The present inventors have conducted various studies on Al alloys for can bodies, and found that increasing the amount of Si in the JIS3004 alloy improves strength and ironing formability, and increasing the amount of Zn increases the amount of pores. We found that food could be reduced. However, ears (jagged edges at the end of the can) become high during ironing and the like, and the ears are trimmed, resulting in a new problem of lowering the production yield.
【0004】そこで、本発明者等は、Siを添加してい
くと耳が高くなる原因を調査し、その原因はSiの増加
により再結晶が抑制されるためであること、再結晶はA
l合金板に分散するMg2 Si化合物の大きさと個数を
規定することにより促進させ得ることを見いだし、さら
に研究を進めて本発明を完成させるに至った。 本発明
は、高強度で、耳が低く、耐孔食性、しごき成形性など
に優れ、2ピースDI缶の薄肉軽量化を実現できる缶胴
用Al合金板およびその製造方法に関する。Therefore, the present inventors investigated the cause of the increase in ear height as Si was added, and found that the cause was that recrystallization was suppressed by the increase of Si.
It has been found that this can be promoted by specifying the size and number of the Mg 2 Si compounds dispersed in the 1 alloy plate, and further research has been carried out to complete the present invention. The present invention relates to an aluminum alloy sheet for a can body, which is high in strength, has low ears, is excellent in pitting corrosion resistance, ironing formability, and the like, and can realize a thin and lightweight two-piece DI can and a method for producing the same.
【0005】[0005]
【課題を解決するための手段】請求項1記載の発明は、
Siを0.3wt%超え0.9wt%以下、Feを0.3〜
0.7wt%、Mnを0.8〜1.4wt%、Cuを0.0
5〜0.5wt%、Mgを0.8〜1.4wt%、Znを
0.25wt%超え1.0wt%以下、Tiを0.01〜
0.1wt%含有し、残部がAlおよび不可避不純物から
なり、Alマトリックス中に径が0.1〜1μmのMg
2 Si化合物が1mm2 あたり10000個以下分散し
ていることを特徴とする缶胴用アルミニウム合金板であ
る。According to the first aspect of the present invention,
More than 0.3 wt% of Si and 0.9 wt% or less,
0.7 wt%, Mn 0.8-1.4 wt%, Cu 0.0
5 to 0.5 wt%, 0.8 to 1.4 wt% of Mg, 0.25 wt% to 1.0 wt% or less of Zn, 0.01 to 0.01 wt% of Ti
0.1 wt%, the balance being Al and unavoidable impurities, and having a diameter of 0.1 to 1 μm in the Al matrix.
An aluminum alloy plate for a can body, wherein 10000 or less 2 Si compounds are dispersed per 1 mm 2 .
【0006】請求項2記載の発明は、Siを0.3wt%
超え0.9wt%以下、Feを0.3〜0.7wt%、Mn
を0.8〜1.4wt%、Cuを0.05〜0.5wt%、
Mgを0.8〜1.4wt%、Znを0.25wt%超え
1.0wt%以下、Tiを0.01〜0.1wt%含有し、
残部がAlおよび不可避不純物からなるAl合金鋳塊に
均質化処理を施し、次いで熱間圧延を圧延終了温度30
0℃〜360℃の条件で施し、次いで焼鈍処理を100
℃/分以上の加熱速度で380℃〜520℃の温度範囲
に昇温し、前記温度範囲に0秒〜2分間保持したのち、
100℃/分以上の冷却速度で冷却して施し、次いで冷
間圧延を施し、その後、必要に応じて仕上焼鈍を施すこ
とを特徴とする請求項1記載の缶胴用アルミニウム合金
板の製造方法である。According to a second aspect of the present invention, there is provided a semiconductor device comprising 0.3 wt% of Si.
Over 0.9 wt% or less, 0.3 to 0.7 wt% Fe, Mn
0.8-1.4 wt%, Cu 0.05-0.5 wt%,
0.8-1.4 wt% Mg, 0.25 wt% or more and 1.0 wt% or less Zn, 0.01-0.1 wt% Ti,
The remaining portion of the Al alloy ingot consisting of Al and inevitable impurities is subjected to a homogenization treatment, and then hot-rolled to a rolling end temperature of 30.
0 ° C. to 360 ° C. and then annealing treatment for 100
After heating to a temperature range of 380 ° C. to 520 ° C. at a heating rate of not less than 0 ° C./min and maintaining the temperature range for 0 second to 2 minutes,
2. The method for producing an aluminum alloy sheet for a can body according to claim 1, wherein the aluminum alloy sheet for a can body is cooled at a cooling rate of 100 ° C./min or more, then subjected to cold rolling, and then subjected to finish annealing as required. It is.
【0007】[0007]
【発明の実施の形態】以下に本発明のアルミニウム合金
板の合金組成について説明する。SiとMgはMg2 S
i化合物を形成して、或いは一部がAlマトリックスに
固溶して強度向上に寄与する。とりわけ、Siは、後述
するFe−Mn系化合物を硬く微細な化合物に変態さ
せ、しごき成形時の耐焼付け性を改善する。Siの含有
量を0.3wt%を超え0.9wt%以下に規定する理由
は、0.3wt%未満ではその効果が十分に得られず、
0.9wt%を超えると冷間圧延後に粗大なMg2 Si化
合物が析出して成形性が低下し、また孔食が発生し易く
なるためである。Mgの含有量を0.8〜1.4wt%に
規定する理由は、0.8wt%未満ではその強度向上効果
が十分に得られず、1.4wt%を超えるとしごき成形性
などが低下するためである。SiとMgの含有量がとも
に多いと、Mg2 Siの個数が増加して焼鈍処理後に十
分に再結晶せず耳が高くなる。DESCRIPTION OF THE PREFERRED EMBODIMENTS The alloy composition of the aluminum alloy sheet of the present invention will be described below. Si and Mg are Mg 2 S
An i-compound is formed or a part of it is dissolved in an Al matrix, thereby contributing to an improvement in strength. In particular, Si transforms a later-described Fe—Mn-based compound into a hard and fine compound, and improves seizure resistance during ironing. The reason for specifying the Si content to be more than 0.3 wt% and 0.9 wt% or less is that if the content is less than 0.3 wt%, the effect cannot be sufficiently obtained.
If the content exceeds 0.9 wt%, a coarse Mg 2 Si compound is precipitated after cold rolling, whereby the formability is reduced and pitting corrosion is liable to occur. The reason for defining the Mg content to be 0.8 to 1.4 wt% is that if the content is less than 0.8 wt%, the strength improving effect cannot be sufficiently obtained, and if the content exceeds 1.4 wt%, iron formability and the like are reduced. That's why. When both the contents of Si and Mg are large, the number of Mg 2 Si increases and the ears become high without being sufficiently recrystallized after the annealing treatment.
【0008】FeとMnはFe−Mn系化合物を形成し
てフランジ成形性を高める。また本発明ではJIS30
04合金よりSiが多く含有されており、このSiの増
分が前述のようにFe−Mn系化合物を硬くかつ微細化
してしごき成形性が改善される。ここで、Feの含有量
を0.3〜0.7wt%、Mnの含有量を0.8〜1.4
wt%に規定する理由は、いずれが下限未満でもフランジ
成形性並びにしごき成形性が十分に向上せず、上限を超
えると初晶巨大化合物が生成して成形性全般が低下する
ためである。[0008] Fe and Mn form an Fe-Mn-based compound to enhance flange formability. In the present invention, JIS30
The alloy contains more Si than the alloy No. 04, and the increment of Si hardens and refines the Fe-Mn-based compound as described above to improve the iron formability. Here, the content of Fe is 0.3 to 0.7 wt%, and the content of Mn is 0.8 to 1.4.
The reason for specifying the wt% is that if any of them is less than the lower limit, the flange formability and the iron formability are not sufficiently improved, and if the upper limit is exceeded, a primary crystal giant compound is formed and the overall formability is reduced.
【0009】CuはAlマトリックスに固溶して強度向
上に寄与する。その含有量を0.05〜0.5wt%に規
定する理由は、0.05wt%未満ではその効果が十分に
得られず、0.5wt%を超えるとしごき成形性およびフ
ランジ成形性が低下するためである。[0009] Cu forms a solid solution in the Al matrix and contributes to improvement in strength. The reason for defining the content to be 0.05 to 0.5 wt% is that if the content is less than 0.05 wt%, the effect cannot be sufficiently obtained, and if it exceeds 0.5 wt%, the iron formability and the flange formability deteriorate. That's why.
【0010】ZnはAlマトリックスに固溶して強度向
上に寄与する。また本発明ではZnがJIS3004合
金より多く含有されており、このZnの増分が、Mg2
Si化合物などを微細化して前記化合物を起点とする孔
食の発生を抑制する。その含有量を0.25wt%を超え
て1.0wt%以下に規定する理由は、0.25wt%以下
ではその効果が十分に得られず、1.0wt%を超えると
成形性が低下し、またMgZn2 化合物が生成して却っ
て孔食が発生し易くなるためである。[0010] Zn forms a solid solution in the Al matrix and contributes to improvement in strength. Further, in the present invention, Zn is contained more than the JIS 3004 alloy, and the increment of Zn is Mg 2
The Si compound or the like is miniaturized to suppress the occurrence of pitting corrosion starting from the compound. The reason why the content is specified to be more than 0.25 wt% and not more than 1.0 wt% is that if the content is less than 0.25 wt%, the effect cannot be sufficiently obtained. Another reason is that the MgZn 2 compound is generated and pitting corrosion easily occurs.
【0011】Tiは鋳造組織を微細化して材料表面の筋
状模様の発生を抑える。その含有量を0.01〜0.1
wt%に規定する理由は、0.01wt%未満ではその効果
が十分に得られず、0.1wt%を超えると初晶巨大化合
物が発生し易くなり各成形性が著しく損なわれるためで
ある。Tiに加えて、Bを0.0001〜0.01wt%
添加すると微細化がさらに促進される。Ti makes the cast structure finer and suppresses the generation of streak patterns on the material surface. The content is 0.01-0.1
The reason for specifying the wt% is that if the amount is less than 0.01% by weight, the effect cannot be sufficiently obtained, and if the amount exceeds 0.1% by weight, a primary crystal giant compound is easily generated and the moldability is significantly impaired. 0.0001-0.01wt% B in addition to Ti
Addition further promotes micronization.
【0012】本発明において、径が0.1〜1μmのM
g2 Si化合物の分散個数を10000個/mm2 以下
に規定する理由は、前記Mg2 Si化合物が10000
個/mm2 以下の場合は焼鈍処理後において完全再結晶
組織となり、耳を低く抑えられるためである。また前記
Mg2 Si化合物の個数を10000個/mm2 以下に
抑えれば、Mg固溶量の減少が0.09wt%以下に、S
i固溶量の減少が0.05wt%以下に抑えられ、固溶M
g、Siによる強度向上効果をそれ程落とさずに済む。In the present invention, M having a diameter of 0.1 to 1 μm
The reason why the number of dispersed g 2 Si compounds is defined to be 10,000 / mm 2 or less is that the Mg 2 Si compound is
If the number of pieces / mm 2 or less, a completely recrystallized structure is obtained after the annealing treatment, and the ears can be kept low. If the number of the Mg 2 Si compounds is suppressed to 10000 / mm 2 or less, the decrease in the amount of solid solution of Mg becomes 0.09 wt% or less,
i The decrease in the amount of solid solution is suppressed to 0.05 wt% or less.
The strength improvement effect of g and Si does not need to be reduced so much.
【0013】次に、本発明のアルミニウム合金板の製造
方法について説明する。本発明の合金板は、例えば、D
C鋳造、均質化処理、熱間圧延、焼鈍処理、冷間圧延、
並びに必要に応じ仕上焼鈍の各工程を順に施して製造さ
れる。以下に各工程について説明する。Next, a method for manufacturing the aluminum alloy sheet of the present invention will be described. The alloy plate of the present invention is, for example, D
C casting, homogenization, hot rolling, annealing, cold rolling,
It is also manufactured by sequentially performing each step of finish annealing as required. Hereinafter, each step will be described.
【0014】均質化処理では、溶質元素の濃度分布が均
一化し、晶出物が再固溶し、またフランジ成形性に有用
なFe−Mn系化合物が生成される。均質化処理は、5
80〜620℃で4〜12時間加熱する条件が、均質化
処理が十分になされ、かつ生産性が阻害されず望まし
い。In the homogenization treatment, the concentration distribution of the solute element is made uniform, the crystallized substance is re-dissolved, and an Fe-Mn compound useful for flange formability is produced. Homogenization treatment is 5
The condition of heating at 80 to 620 ° C. for 4 to 12 hours is preferable because the homogenization treatment is sufficiently performed and the productivity is not hindered.
【0015】本発明において、熱間圧延は粗圧延と仕上
圧延とからなり、熱間圧延後にMg 2 Si化合物が析出
し、また再結晶が起きる。このときの再結晶率が80%
以上だと、次の焼鈍処理後に完全再結晶組織となり、し
ごき成形時などで耳が低くなる。前記熱間圧延の終了温
度を300〜360℃に規定する理由は、300℃未満
では再結晶率80%以上の組織が得られず、360℃を
超えると得られるAl合金板の表面性状が悪化するため
である。In the present invention, hot rolling includes rough rolling and finishing.
Rolling, and after hot rolling Mg TwoSi compound precipitates
And recrystallization occurs. Recrystallization rate at this time is 80%
With the above, a completely recrystallized structure is obtained after the next annealing treatment, and
Ears become low during molding. End temperature of the hot rolling
The reason why the temperature is specified at 300 to 360 ° C is less than 300 ° C.
In this case, a structure with a recrystallization rate of 80% or more cannot be obtained.
If it exceeds, the surface properties of the obtained Al alloy sheet will deteriorate.
It is.
【0016】熱間圧延後に析出したMg2 Si化合物
は、その後の焼鈍処理で一部がAlマトリックス中に再
固溶し、この再固溶により0.1〜1μmの大きさのM
g2 Siが1mm2 あたり10000個以下に減少して
再結晶が促進し、完全再結晶組織が得られる。前記焼鈍
処理を、380〜520℃で0秒〜2分間保持し、加熱
および冷却速度を100℃/分以上に規定して施す理由
は、焼鈍処理温度が380℃未満ではMg2 Si化合物
の再固溶量が不十分で、径が0.1〜1μmのMg2 S
i化合物が10000個/mm2 を超えて分散するため
完全再結晶組織が得られず、焼鈍処理温度が520℃を
超えても保持時間が2分を超えても結晶粒が粗大化して
しごき成形性などが低下し、また加熱速度または冷却速
度のいずれが100℃/分未満でも生産性が低下し、特
に冷却速度が100℃/分未満では、冷却時にMg2 S
i化合物が多数析出するためである。The Mg 2 Si compound precipitated after hot rolling partially re-dissolves in the Al matrix in the subsequent annealing treatment, and the re-solid solution causes M 2 having a size of 0.1 to 1 μm.
g 2 Si is reduced to 10,000 or less per 1 mm 2, recrystallization is promoted, and a completely recrystallized structure is obtained. The reason why the annealing treatment is performed at 380 to 520 ° C. for 0 second to 2 minutes and the heating and cooling rate is specified to be 100 ° C./min or more is that when the annealing treatment temperature is lower than 380 ° C., the Mg 2 Si compound is re-used. Insufficient solid solution, 0.1 to 1 μm in diameter of Mg 2 S
Since the i-compound is dispersed in excess of 10,000 particles / mm 2 , a complete recrystallized structure cannot be obtained, and even if the annealing temperature exceeds 520 ° C or the holding time exceeds 2 minutes, the crystal grains become coarse and ironing is performed. If the heating rate or the cooling rate is less than 100 ° C./min, the productivity is reduced. In particular, if the cooling rate is less than 100 ° C./min, Mg 2 S
This is because a large number of i-compounds are precipitated.
【0017】本発明において、冷間圧延はしぼり成形な
どで必要な強度を付与するために行う。冷間圧延率が6
0%未満では十分な強度が得られず、90%を超えると
しごき成形で耳が高くなる。従って冷間圧延率は60〜
90%が望ましい。In the present invention, the cold rolling is performed to impart necessary strength by squeezing or the like. Cold rolling rate is 6
If it is less than 0%, sufficient strength cannot be obtained, and if it exceeds 90%, the ears become high due to ironing. Therefore, the cold rolling rate is 60-
90% is desirable.
【0018】本発明では、冷間圧延後、必要に応じて仕
上焼鈍を施して伸びを回復させる。これは冷間圧延後の
引張強度が損なわれない条件、例えば120℃以下の低
温で3hr以下の条件で施すのが望ましい。In the present invention, after cold rolling, finish annealing is performed as necessary to recover elongation. This is desirably performed under conditions where the tensile strength after cold rolling is not impaired, for example, at a low temperature of 120 ° C. or lower and 3 hours or less.
【0019】[0019]
【実施例】以下に本発明を実施例により詳細に説明す
る。 (実施例1)表1に示す組成のAl合金鋳塊(厚さ50
0mm)に600℃で6時間の均質化処理を施し、次い
で熱間圧延(粗圧延→仕上圧延)を圧延終了温度330
℃で施して厚さ2.2mmの熱延材(熱延コイル)と
し、この熱延材を室温に冷却したのち、連続焼鈍炉で4
00℃で0秒間(400℃に到達後直ちに空冷)焼鈍処
理した。この焼鈍処理での加熱速度または冷却速度はそ
れぞれ850℃/分、1000℃/分とした。焼鈍処理
後、厚さ0.3mmに冷間圧延(圧延率86.4%)
し、次いで115℃で2時間仕上焼鈍して缶胴用Al合
金板を製造した。The present invention will be described below in detail with reference to examples. (Example 1) An Al alloy ingot having a composition shown in Table 1 (thickness: 50)
0 mm) at 600 ° C. for 6 hours, followed by hot rolling (rough rolling → finishing rolling) at a rolling end temperature of 330 ° C.
C. to form a hot-rolled material (hot-rolled coil) having a thickness of 2.2 mm. After cooling this hot-rolled material to room temperature, it is heated in a continuous annealing furnace for 4 hours.
An annealing treatment was performed at 00 ° C. for 0 second (air cooling immediately after reaching 400 ° C.). The heating rate or cooling rate in this annealing treatment was 850 ° C./min and 1000 ° C./min, respectively. After annealing, cold-rolled to a thickness of 0.3 mm (rolling rate 86.4%)
Then, finish annealing was performed at 115 ° C. for 2 hours to produce an Al alloy plate for a can body.
【0020】実施例1で得られた各々のAl合金板につ
いて、耳率、引張強度、缶の成形性、Mg2 S
i化合物の大きさと個数、孔食の発生状況を調べた。
耳率は、前記Al合金板から直径57mmの円板を切
出し、これを直径33mm、肩R2.5mmのポンチを
用いクリアランス30%で深しぼりしたときの缶の高さ
に対する耳の平均高さの割合(耳率)で表した。引張
強度は、JISZ2241に準じて、引張強さ(TS)
と0.2%耐力(YS)を測定した。塗装焼付け条件
(200℃×20分)で加熱処理したものについても測
定した。缶の成形性は、炭酸飲料用のDI缶胴(内径
66mm、側壁板厚103μm、側壁先端部板厚165
μm、ネック部の内径57mm、ネック部段数4段、フ
ランジ幅2.2mm)を多数製缶し、そのときの破胴
率、表面性状、フランジ割れを調べた。Mg2 Si化
合物の大きさと個数はTEM観察と画像処理により測定
した。孔食の発生状況は缶側壁から切出した20×8
0mmの試験片を40℃の1%クエン酸+0.1%Na
Cl溶液に1週間浸漬したのちの試験片の表面を観察し
て調べた。孔食深さが全て20μm未満のものは良好
(○)、孔食深さが20μmを超えるものが含まれるも
のは不良(×)と判定した。結果を表2に示す。For each of the Al alloy plates obtained in Example 1, the ear ratio, tensile strength, moldability of the can, Mg 2 S
The size and number of i-compounds and the occurrence of pitting corrosion were examined.
The ear ratio was determined by cutting out a disk having a diameter of 57 mm from the Al alloy plate and squeezing the disk with a punch having a diameter of 33 mm and a shoulder R of 2.5 mm with a clearance of 30%. It was expressed as a percentage (ear ratio). Tensile strength is the tensile strength (TS) according to JISZ2241.
And 0.2% proof stress (YS) were measured. Measurements were also made on those subjected to heat treatment under the conditions of baking paint (200 ° C. × 20 minutes). The moldability of the can was measured using a DI can body for carbonated beverages (inner diameter 66 mm, side wall thickness 103 μm, side wall thickness 165).
μm, an inner diameter of a neck portion of 57 mm, a number of steps of a neck portion of 4 steps, and a flange width of 2.2 mm) were manufactured in many cans, and the fracture rate, surface properties, and flange cracking at that time were examined. The size and number of the Mg 2 Si compound were measured by TEM observation and image processing. The occurrence of pitting is 20 × 8 cut out from the side wall of the can.
A 0 mm test piece was treated with 1% citric acid + 0.1% Na at 40 ° C.
After immersing in a Cl solution for one week, the surface of the test piece was observed and examined. Samples with a pit depth of less than 20 μm were judged as good (○), and samples with a pit depth of more than 20 μm were judged as poor (×). Table 2 shows the results.
【0021】[0021]
【表1】 (注)単位:wt%。[Table 1] (Note) Unit: wt%.
【0022】[0022]
【表2】 (注)単位:wt%。[Table 2] (Note) Unit: wt%.
【0023】[0023]
【表3】 (注)MPa。45度耳、絶対値が大きい程耳が高い。 破胴率 ppm、性状:○良好, ×焼付け発生、割れ:フランジ割れ ppm。[Table 3] (Note) MPa. The 45-degree ear, the higher the absolute value, the higher the ear. Fracture ratio ppm, properties: good, x burning occurred, crack: flange crack ppm.
【0024】[0024]
【表4】 (注)MPa。45度耳、絶対値が大きい程耳が高い。 破胴率 ppm、性状:○良好, ×焼付け発生、割れ:フランジ割れ ppm。[Table 4] (Note) MPa. The 45-degree ear, the higher the absolute value, the higher the ear. Fracture ratio ppm, properties: good, x burning occurred, crack: flange crack ppm.
【0025】表3、4より明らかなように、本発明例(N
o.A〜D) はいずれも引張強度が高く、耳率が低く
(2.5%以内)、缶の成形性が良好で孔食も発生しな
かった。これに対し、比較例(No.E〜Q) は、いずれも
合金元素のいずれかが本発明規定値外のため、前記特性
のいずれかが低下して実用性に欠けた。特に No.FはM
g2 Siの個数が多かったため耳率が極めて高くなっ
た。As is clear from Tables 3 and 4, the present invention example (N
o.A to D) all had high tensile strength, low ear ratio (within 2.5%), good moldability of the can, and no pitting. On the other hand, in Comparative Examples (Nos. E to Q), any one of the alloy elements was out of the range specified in the present invention, so that any one of the above characteristics was deteriorated and lacked practicality. Especially No.F is M
The ear ratio was extremely high due to the large number of g 2 Si.
【0026】(実施例2)実施例1に示す本発明規定組
成の合金Bの鋳塊(厚さ500mm)に600℃で6時
間の均質化処理を施し、次いで熱間圧延して厚さ2.2
mmの熱延材(熱延コイル)とし、この熱延材を室温ま
で冷却したのち、連続焼鈍炉を用いて焼鈍処理し、その
後、厚さ0.3mmに冷間圧延(圧延率:86.4%)
し、次いで115℃で2時間仕上焼鈍して缶胴用Al合
金板を製造した。熱間圧延終了温度および焼鈍処理条件
は表5に示すように種々に変化させた。このようにして
得られた合金板について実施例1と同じ方法により種々
特性を調査した。結果を表6に示す。(Example 2) An ingot (thickness: 500 mm) of the alloy B having the composition specified in the present invention shown in Example 1 was subjected to a homogenization treatment at 600 ° C for 6 hours and then hot-rolled to a thickness of 2 mm. .2
mm hot-rolled material (hot-rolled coil), and after the hot-rolled material is cooled to room temperature, is annealed using a continuous annealing furnace, and then cold-rolled to a thickness of 0.3 mm (rolling ratio: 86.000 mm). 4%)
Then, finish annealing was performed at 115 ° C. for 2 hours to produce an Al alloy plate for a can body. The hot rolling end temperature and annealing conditions were variously changed as shown in Table 5. Various characteristics of the alloy plate thus obtained were investigated in the same manner as in Example 1. Table 6 shows the results.
【0027】[0027]
【表5】 [Table 5]
【0028】[0028]
【表6】 (注)MPa。45度耳、絶対値が大きい程耳が高い。 破胴率 ppm、性状:○良好, ×焼付け発生、割れ:フランジ割れ ppm。[Table 6] (Note) MPa. The 45-degree ear, the higher the absolute value, the higher the ear. Fracture ratio ppm, properties: good, x burning occurred, crack: flange crack ppm.
【0029】表6より明らかなように、本発明例 (No.1
〜4)は、いずれも引張強度が高く、耳率が低く(2.5
%以内)、缶の成形性が良好で、孔食も発生しなかっ
た。これに対し、比較例のNo.5は熱間圧延終了温度が低
いため、No.7は焼鈍処理温度が低いため、 No.10は昇温
速度と冷却速度が低いため、いずれもMg2 Si化合物
の個数が多くなり、その結果、耳率が高くなり、引張強
度が低下した。No.6は熱間圧延終了温度が高いため、N
o.8は焼鈍処理温度が高いため、No.9は焼鈍処理時間が
長いため、いずれも結晶粒が粗大化して成形性が悪化し
た。As is clear from Table 6, the present invention example (No. 1)
4) have high tensile strength and low ear ratio (2.5%).
%), The moldability of the can was good, and no pitting occurred. In contrast, since No.5 lower end of hot rolling temperature of the comparative example, since No.7 is annealing temperature is low, No.10, because the heating rate and the cooling rate is low, both Mg 2 Si The number of compounds increased, resulting in a higher ear rate and lower tensile strength. No. 6 has a high hot rolling end temperature,
In the case of o.8, the annealing temperature was high, and in the case of No.9, the annealing time was long, and in each case, the crystal grains became coarse and the formability deteriorated.
【0030】[0030]
【発明の効果】以上に述べたように、本発明の缶胴用A
l合金板は、JIS3004合金のSiとZnを増量さ
せ、前記SiによりFe−Mn系化合物を硬くかつ微細
化してしごき成形性を向上させ、前記Znにより孔食を
改善し、さらにMg2 Si化合物の析出個数を規制して
強度向上と耳発生の抑制を図ったもので、DI缶の薄肉
軽量化を実現できる。また前記Al合金板は、熱間圧延
終了温度と焼鈍処理条件を規定した常法により容易に製
造できる。As described above, the can body A according to the present invention is used.
1 alloy plate increases the amount of Si and Zn of the JIS 3004 alloy, hardens and refines the Fe-Mn-based compound by the Si to improve ironing formability, improves the pitting corrosion by the Zn, and further improves the Mg 2 Si compound. The number of precipitates is regulated to improve the strength and suppress the generation of ears, so that the DI can can be made thinner and lighter. Further, the Al alloy plate can be easily manufactured by an ordinary method in which a hot rolling end temperature and annealing conditions are specified.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 FI テーマコート゛(参考) C22F 1/00 630 C22F 1/00 630K 630A 640 640A 673 673 683 683 684 684C 691 691A 691C 691B 692 692A 694 694B ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference)
Claims (2)
Feを0.3〜0.7wt%、Mnを0.8〜1.4wt
%、Cuを0.05〜0.5wt%、Mgを0.8〜1.
4wt%、Znを0.25wt%超え1.0wt%以下、Ti
を0.01〜0.1wt%含有し、残部がAlおよび不可
避不純物からなり、Alマトリックス中に径が0.1〜
1μmのMg2 Si化合物が1mm2 あたり10000
個以下分散していることを特徴とする缶胴用アルミニウ
ム合金板。Claims 1. An alloy containing Si in an amount of more than 0.3 wt% and not more than 0.9 wt%.
0.3 to 0.7 wt% of Fe and 0.8 to 1.4 wt% of Mn
%, 0.05 to 0.5% by weight of Cu, and 0.8 to 1% of Mg.
4 wt%, Zn over 0.25 wt% and 1.0 wt% or less, Ti
0.01 to 0.1 wt%, the balance being Al and unavoidable impurities, and having a diameter of 0.1 to 0.1 in the Al matrix.
1 μm of Mg 2 Si compound is 10000 / mm 2
An aluminum alloy plate for a can body, which is dispersed in pieces.
Feを0.3〜0.7wt%、Mnを0.8〜1.4wt
%、Cuを0.05〜0.5wt%、Mgを0.8〜1.
4wt%、Znを0.25wt%超え1.0wt%以下、Ti
を0.01〜0.1wt%含有し、残部がAlおよび不可
避不純物からなるAl合金鋳塊に均質化処理を施し、次
いで熱間圧延を圧延終了温度300℃〜360℃の条件
で施し、次いで焼鈍処理を100℃/分以上の加熱速度
で380℃〜520℃の温度範囲に昇温し、前記温度範
囲に0秒〜2分間保持したのち、100℃/分以上の冷
却速度で冷却して施し、次いで冷間圧延を施し、その
後、必要に応じて仕上焼鈍を施すことを特徴とする請求
項1記載の缶胴用アルミニウム合金板の製造方法。2. The method according to claim 1, wherein the content of Si is more than 0.3 wt% and 0.9 wt% or less;
0.3 to 0.7 wt% of Fe and 0.8 to 1.4 wt% of Mn
%, 0.05 to 0.5% by weight of Cu, and 0.8 to 1% of Mg.
4 wt%, Zn over 0.25 wt% and 1.0 wt% or less, Ti
, A homogenization treatment is applied to an Al alloy ingot consisting of Al and inevitable impurities, and hot rolling is performed at a rolling end temperature of 300 ° C to 360 ° C. The temperature of the annealing treatment is raised to a temperature range of 380 ° C. to 520 ° C. at a heating rate of 100 ° C./min or more, and maintained at the above temperature range for 0 second to 2 minutes, and then cooled at a cooling rate of 100 ° C./min or more. 2. The method for producing an aluminum alloy sheet for a can body according to claim 1, wherein the aluminum alloy sheet is subjected to cold rolling, followed by finish annealing as necessary.
Priority Applications (1)
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---|---|---|---|
JP16974098A JP2000001730A (en) | 1998-06-17 | 1998-06-17 | Aluminum alloy sheet for can body, and its production |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16974098A JP2000001730A (en) | 1998-06-17 | 1998-06-17 | Aluminum alloy sheet for can body, and its production |
Publications (1)
Publication Number | Publication Date |
---|---|
JP2000001730A true JP2000001730A (en) | 2000-01-07 |
Family
ID=15891976
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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JP16974098A Pending JP2000001730A (en) | 1998-06-17 | 1998-06-17 | Aluminum alloy sheet for can body, and its production |
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Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103781927A (en) * | 2012-01-31 | 2014-05-07 | 爱信轻金属株式会社 | High-strength aluminum alloy extrudate with excellent corrosion resistance, ductility, and hardenability and process for producing same |
CN109266888A (en) * | 2018-12-03 | 2019-01-25 | 东北轻合金有限责任公司 | A kind of 308 alloy cast ingot and its preparation method and application |
CN111074107A (en) * | 2019-12-26 | 2020-04-28 | 河南明泰科技发展有限公司 | 3004 aluminum foil and preparation method and application thereof |
CN111663061A (en) * | 2020-06-23 | 2020-09-15 | 江苏大学 | Method for preparing Al-Si alloy grain refiner |
WO2024054235A1 (en) * | 2022-09-09 | 2024-03-14 | Novelis Inc. | Rapid annealing and quenching of aluminum alloy products to reduce roping or ludering |
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1998
- 1998-06-17 JP JP16974098A patent/JP2000001730A/en active Pending
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103781927A (en) * | 2012-01-31 | 2014-05-07 | 爱信轻金属株式会社 | High-strength aluminum alloy extrudate with excellent corrosion resistance, ductility, and hardenability and process for producing same |
CN103781927B (en) * | 2012-01-31 | 2017-02-08 | 爱信轻金属株式会社 | High-strength aluminum alloy extrudate with excellent corrosion resistance, ductility, and hardenability and process for producing same |
CN109266888A (en) * | 2018-12-03 | 2019-01-25 | 东北轻合金有限责任公司 | A kind of 308 alloy cast ingot and its preparation method and application |
CN111074107A (en) * | 2019-12-26 | 2020-04-28 | 河南明泰科技发展有限公司 | 3004 aluminum foil and preparation method and application thereof |
CN111663061A (en) * | 2020-06-23 | 2020-09-15 | 江苏大学 | Method for preparing Al-Si alloy grain refiner |
WO2024054235A1 (en) * | 2022-09-09 | 2024-03-14 | Novelis Inc. | Rapid annealing and quenching of aluminum alloy products to reduce roping or ludering |
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