JP3226775B2 - Method for producing steel sheet for DI can with excellent necked-in workability - Google Patents
Method for producing steel sheet for DI can with excellent necked-in workabilityInfo
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- JP3226775B2 JP3226775B2 JP34177995A JP34177995A JP3226775B2 JP 3226775 B2 JP3226775 B2 JP 3226775B2 JP 34177995 A JP34177995 A JP 34177995A JP 34177995 A JP34177995 A JP 34177995A JP 3226775 B2 JP3226775 B2 JP 3226775B2
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- neck
- steel sheet
- steel
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、ＤＩ缶でのネッキ
ング加工性に優れたぶりきなどの表面処理が施された容
器用鋼板を製造する方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a steel sheet for a container which has been subjected to a surface treatment such as tinplate which is excellent in necking workability in a DI can.
【０００２】[0002]
【従来の技術】ジュース、ビールなどの内圧のかかる飲
料缶においては、現在、絞り加工の後にしごき加工を行
うＤＩ（Ｄｒａｗｎ ａｎｄ Ｉｒｏｎｅｄ）法によっ
て製造されたＤＩ缶が広く使用されている。このＤＩ缶
の缶胴のネック加工には、図３に示すダイネック法、図
４に示すスピンネック法などがあるが、いずれも缶端の
口径を小さくする一種の口絞り加工を行い、後工程で缶
胴よりも、径の小さい蓋を取り付けることが特徴であ
る。この口絞り加工時に、円周方向の圧縮応力によって
材料が座屈し、ネック部にしわが発生する場合がある。
このしわは、外観を害するだけでなく、蓋を取り付けた
後の密封性を悪くし、内容物の濡れを発生させる可能性
がある。よってこのネックしわを防止することは、製缶
メーカにとって重要な課題となっている。2. Description of the Related Art In beverage cans, such as juices and beers, which are subject to internal pressure, DI cans manufactured by the DI (Drawn and Ironed) method in which ironing is performed after drawing are widely used. The necking of the body of the DI can includes a die necking method shown in FIG. 3 and a spin necking method shown in FIG. 4. The feature is that a lid smaller in diameter than the can body is attached. During this drawing process, the material may buckle due to compressive stress in the circumferential direction, and wrinkles may occur in the neck portion.
The wrinkles not only impair the appearance, but also impair the sealing after the lid is attached, and may cause the contents to be wet. Therefore, preventing such neck wrinkles is an important issue for can makers.
【０００３】一方、近年、蓋のコストを削減するため、
製缶メーカでは、蓋の径小化が進んできている。ところ
が、蓋の径小化が進むと、缶胴の口絞り加工率が大きく
なるため、上述したネックしわが発生しやすくなる。し
たがって蓋の径小化を達成するために、ネック加工性に
優れた鋼板を開発することが、鉄鋼メーカにとって重要
な課題となっている。さて、このネックしわを抑制する
ためには、従来より、経験的に軟質な鋼板が有利である
ことが知られている。例えば、特開平５−２８７４４３
号公報では、Ｃが０．００３以上０．０１％以下でＴｉ
等を添加した鋼板が、軟質で、ネックドイン加工性に優
れることが記載されている。しかしこのような高純な鋼
板は、鋼板の製造コストが高くなることや、飲料缶での
耐食性が確認されていないことなどから、飲料缶用に
は、現在適用されていない。On the other hand, recently, in order to reduce the cost of the lid,
In can makers, the diameter of the lid has been reduced. However, as the diameter of the lid is reduced, the neck drawing rate of the can body increases, so that the above-described neck wrinkles are likely to occur. Therefore, in order to reduce the diameter of the lid, it is an important issue for steel manufacturers to develop a steel sheet having excellent neck workability. Now, it has been empirically known that a soft steel plate is advantageous for suppressing this neck wrinkle. For example, Japanese Patent Application Laid-Open No. 5-287443
In the publication, when C is 0.003 or more and 0.01% or less, Ti
It is described that the steel sheet to which the steel is added is soft and has excellent necked-in workability. However, such a high-purity steel sheet is not currently used for beverage cans because the production cost of the steel sheet is high and corrosion resistance in beverage cans has not been confirmed.
【０００４】また、特開昭６３−３３５２２号公報で
は、鋼成分が、Ｃ：０．０１〜０．０６％、Ｎ：０．０
０７０％以下、酸可溶Ａｌ０．００５〜０．０８％で、
本願発明の鋼成分と部分的に重複する「ＤＩ缶加工用Ｔ
−１ないしＴ−３級軟質表面処理用原板の製造法」が記
載されている。このＣが０．０１％以上の鋼で、しわに
有利な軟質なＴ−１の鋼板を得るためには、実際には、
７５０℃超の高温焼鈍が必要であった。ところが、７５
０℃超の焼鈍温度では、セメンタイトが凝集化するた
め、フランジ成形時にフランジ割れが多発するという問
題があった。このため、実際には焼鈍温度は７５０℃以
下で製造し、耐ネックしわ性の悪いＴ−２以上の材質し
か得られなかった。よってこの成分系で、ネックしわを
抑制するためには、テンパー度以外のネックしわ支配因
子の究明と、それに伴う成分の絞り込み、製造条件の再
検討が必要であった。[0004] In Japanese Patent Application Laid-Open No. 63-33522, the steel components are C: 0.01 to 0.06% and N: 0.0
070% or less, acid-soluble Al 0.005 to 0.08%,
"T for DI can processing" which partially overlaps with the steel component of the present invention
Production Method of Raw Sheet for Soft Surface Treatment of Class -1 to T-3 ". In order to obtain a soft T-1 steel sheet that is advantageous for wrinkles with steel having C of 0.01% or more, actually,
High temperature annealing above 750 ° C. was required. However, 75
At an annealing temperature higher than 0 ° C., cementite is agglomerated, so that there has been a problem that flange cracking frequently occurs during flange forming. For this reason, in actuality, an annealing temperature of 750 ° C. or lower was produced, and only a material of T-2 or higher having poor neck wrinkle resistance was obtained. Therefore, in order to suppress neck wrinkles in this component system, it was necessary to investigate factors controlling neck wrinkles other than the temper degree, narrow down the components involved, and reexamine the manufacturing conditions.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、Ｃが０．０
１％超で、ＤＩ缶のネックキング成形性に優れており、
ネックしわが発生しないブリキなどの表面処理が施され
た容器用鋼板を提供することを目的とする。According to the present invention, C is 0.0
Exceeding 1%, it is excellent in the neck king formability of DI can,
An object of the present invention is to provide a steel plate for a container which has been subjected to a surface treatment such as tinplate which does not cause neck wrinkles.
【０００６】[0006]
【課題を解決するための手段】本発明は上記問題を解決
するため、成分含有量、熱延での製造条件、焼鈍条件、
焼鈍後の圧延条件等について総合的に検討し、本発明を
見い出したものである。すなわち、本発明の要旨は下記
の通りである。 （１）重量％として、 Ｃ ：０．０２％以上０．０３％以下 Ｍｎ：０．３０％以下 Ｐ ：０．０２５％以下 Ｓ ：０．０２５％以下 ｓｏｌ．Ａｌ：０．０２３２ log（〔Ｎ％〕＋０．０
１）＋０．１１６％以上０．１００％以下 Ｎ ：０．００４０％以下 Ｔ．Ｏ：０．００７０％以下 残部がＦｅ及び不可避的不純物からなる鋼より製造さ
れ、板面のＬ、Ｄ、Ｃ方向の各ｒ値の中で最も低いｒ値
が１．２以上であり、ネック成形時の耐しわ性に優れる
ことを特徴とするＤＩ缶用鋼板。In order to solve the above-mentioned problems, the present invention provides a method for manufacturing a hot rolled steel, comprising:
The present invention has been found by comprehensively studying the rolling conditions and the like after annealing. That is, the gist of the present invention is as follows. (1) As weight%, C: 0.02% or more and 0.03% or less Mn: 0.30% or less P: 0.025% or less S: 0.025% or less sol. Al: 0.0232 log ([N%] + 0.0
1) + 0.116% or more and 0.100% or less N: 0.0040% or less O: 0.0070% or less Manufactured from steel with the balance being Fe and unavoidable impurities, the lowest r value among the r values in the L, D, and C directions of the plate surface is 1.2 or more, and the neck is A steel sheet for DI cans characterized by having excellent wrinkle resistance during molding.
【０００７】（２）重量％として、 Ｃ ：０．０２％以上０．０３％以下 Ｍｎ：０．３０％以下 Ｐ ：０．０２５％以下 Ｓ ：０．０２５％以下 ｓｏｌ．Ａｌ：０．０２３２ log（〔Ｎ％〕＋０．０
１）＋０．１ １６％以上０．１００％以下 Ｎ ：０．００４０％以下 Ｔ．Ｏ：０．００７０％以下 残部がＦｅ及び不可避的不純物からなる鋼を連続鋳造
し、その後、８９０℃以上９５０℃以下で仕上圧延し、
Ａｒ3 変態時の冷却速度を５０℃／ｓ以下で冷却した
後、６９０℃以上７５０℃以下で巻取り、その後、酸
洗、冷延を行い、６９０℃以上７５０℃以下で連続焼鈍
し、１％以上１０％以下の圧延を行い、板面のＬ、Ｄ、
Ｃ方向の各ｒ値の中で最も低いｒ値が１．２以上であ
り、ネック成形時の耐しわ性に優れることを特徴とする
ＤＩ缶用鋼板の製造方法である。(2) As% by weight, C: 0.02% or more and 0.03% or less Mn: 0.30% or less P: 0.025% or less S: 0.025% or less sol. Al: 0.0232 log ([N%] + 0.0
1) +0.1 16% or more and 0.100% or less N: 0.0040% or less O: 0.0070% or less Continuous casting of steel whose balance is Fe and unavoidable impurities, and then finish rolling at 890 ° C or more and 950 ° C or less,
After cooling at a cooling rate of 50 ° C./s or less at the time of Ar 3 transformation, winding is performed at 690 ° C. or more and 750 ° C. or less, followed by pickling and cold rolling, and continuous annealing at 690 ° C. or more and 750 ° C. or less. % Or more and 10% or less is rolled, and L, D,
This is a method for producing a steel sheet for a DI can, characterized in that the lowest r value among the r values in the C direction is 1.2 or more, and the wrinkle resistance during neck forming is excellent.
【０００８】本発明者らは、ネックしわを回避するに
は、従来より知られている軟質化に加え、板面内で最も
ｒ値の低い方向のｒ値（ｒmin ）を向上させることが有
効なことを発見した。この高ｒ値化がしわ抑制に有効な
理由は明らかではないが、高ｒ値化により、材料の座屈
応力が向上したため、しわが発生する時の応力値が大き
くなり、しわが発生しにくくなったのではないかと推定
される。では、このｒmin を向上させる方法について以
下に説明する。図５は、Ｃが０．０２％で本発明の対策
が取られていない鋼（以下従来鋼という）の冷延率とΔ
ｒ〔＝｛（ｒL ＋ｒC ）−２ｒD ｝／２〕の関係を示し
ている。ＤＩ缶用途の鋼板は、板厚が非常に薄いので、
冷延率は９０％程度と非常に大きくなり、ΔｒはＤ方向
のｒ値（ｒD ）が高い負の値となる。この従来鋼で冷延
率９０％の鋼板の板面の各方向のｒ値を図６に示す。従
来鋼では、特にＬ方向のｒ値（ｒL ）が非常に小さいこ
とがわかる。ここで、Ｌ方向とは鋼板の長手方向（圧延
方向）を、Ｃ方向とは鋼板の幅方向（圧延方向と直角方
向）を、Ｄ方向とはＬ方向から４５度の方向（Ｃ方向か
らも４５度の方向）を指します。また、Ｌ方向のｒ値と
は、試験片の長手方向（引張り方向）がＬ方向となるよ
うに切り出した引張試験片を用いて引張試験によって求
めたｒ値をいう。Ｃ、Ｄ方向のｒ値についても同様で
す。 To avoid neck wrinkles, the present inventors have to improve the r value (r min ) in the direction of the lowest r value in the plate surface in addition to the conventionally known softening. I found something useful. It is not clear why this higher r-value is effective in suppressing wrinkles, but since the higher r-value has improved the buckling stress of the material, the stress value when wrinkles occur increases, and wrinkles hardly occur. It is presumed that it has become. Now, a method for improving this r min will be described below. FIG. 5 shows the cold-rolling ratio and Δ of a steel having C of 0.02% and not taking the measures of the present invention (hereinafter referred to as conventional steel).
r [= {(r L + r C ) −2r D } / 2]. Since the steel plate for DI can is very thin,
The cold rolling reduction is as large as about 90%, and Δr is a negative value having a high r value (r D ) in the D direction. FIG. 6 shows r values in each direction of the sheet surface of the conventional steel sheet having a cold rolling rate of 90%. It can be seen that the conventional steel has a very small r value (r L ) in the L direction. Here, the L direction is the longitudinal direction of the steel sheet (rolled
Direction), the C direction is the width direction of the steel sheet (the direction perpendicular to the rolling direction)
Direction) is a direction 45 degrees from the L direction (C direction
Also indicate the direction of 45 degrees). Also, the r value in the L direction and
Means that the longitudinal direction (tensile direction) of the test piece is the L direction
Using a tensile test piece cut out
The r value. The same applies to the r values in the C and D directions.
You.
【０００９】本発明者らは、Δｒを小さくし、板面内の
ｒ値の異方性を改善すると同時に、ｒ〔＝（ｒL ＋ｒC
＋２ｒD ）／４〕値（以下、ｒはここでは深絞り特性の
指標となるｒ値の面内平均値を示す）を向上させること
で、このｒL （ｒmin ）を大幅に向上することに成功し
た。では、低Δｒ化と高ｒ化を同時に達成する製造上の
ポイントについて以下に説明する。まず、低Δｒ化は、
熱延の圧延温度を８９０℃以上の高温で圧延し、さら
に、圧延後にＡｒ3 変態時の冷却速度が５０℃／ｓ以下
の緩冷却を行い、熱延板の粒径を大きくすることで達成
した。なお、熱延板粒径が粗大化すると、Δｒが小さく
なるのは、焼鈍時に粒内の変形態より、Ｄ方向のｒ値を
弱める｛１１０｝＜００１＞がでやすくなり、Δｒが負
の値から０に近づいたためと思われる。次に高ｒ値化
は、熱延での高温巻き取りと、高温焼鈍化により、焼鈍
時の粒成長を促進することにより得られる。高温巻き取
りにより、焼鈍時の粒成長が促進されるのは、巻取り時
のＡｌＮの析出促進により、熱延板に固溶Ｎがほとんど
残存せず、焼鈍時に粒成長を抑制する微細なＡｌＮが発
生しないためと考えられる。The present inventors have made it possible to reduce Δr and improve the anisotropy of the r value in the plate surface, and at the same time, r [= (r L + r C
+ 2r D ) / 4] (herein, r indicates an in-plane average value of r value as an index of the deep drawing characteristic), thereby greatly improving this r L (r min ). succeeded in. In the following, the points in production that simultaneously achieve a low Δr and a high r will be described. First, low Δr is
Achieved by rolling at a hot rolling temperature of 890 ° C or higher, and then performing slow cooling at a cooling rate of 50 ° C / s or less at the time of Ar 3 transformation after rolling to increase the grain size of the hot-rolled sheet. did. When the hot-rolled sheet grain size is coarsened, Δr decreases because {110} <001> that weakens the r-value in the D direction is more likely to occur than in-grain deformation during annealing, and Δr is negative. This is probably because the value approached zero. Next, a higher r-value is obtained by accelerating grain growth during annealing by high-temperature winding in hot rolling and high-temperature annealing. The high temperature winding promotes the grain growth during annealing because the precipitation of AlN at the time of winding hardly causes solid solution N to remain in the hot-rolled sheet, and the fine AlN that suppresses the grain growth during annealing. It is considered that no problem occurs.
【００１０】では、以下に本発明について詳細に述べ
る。Ｃはネック成形性に大きく影響を与える元素であ
る。Ｃが０．０３％超となれば、焼鈍時の粒成長が小さ
く、高いｒmin 値が得られず、ネック成形時にしわが発
生するので、Ｃは０．０３％以下とした。また、Ｃが
０．０２％未満となれば製鋼の脱ガスコストが高くなる
ので、下限を０．０２％とした。Ｍｎ、Ｐ、Ｓは材質を
硬化させるだけでなく、これらの元素を加えると、鋼板
の耐食性を劣化させるので、上限をＭｎは０．３０％、
Ｐは０．０２５％、Ｓは０．０２５％とした。Now, the present invention will be described in detail below. C is an element that greatly affects neck formability. If C exceeds 0.03%, the grain growth during annealing is small, a high r min value cannot be obtained, and wrinkles occur during neck molding, so C was set to 0.03% or less. Further, if C is less than 0.02%, the degassing cost of steelmaking increases, so the lower limit was made 0.02%. Mn, P, and S not only harden the material, but when these elements are added, the corrosion resistance of the steel sheet is deteriorated.
P was 0.025% and S was 0.025%.
【００１１】ｓｏｌ．Ａｌは、０．１００％超となる
と、Ａｌ2 Ｏ3 系介在物が増えて、フランジ成形時に割
れが発生するため、上限を０．１００％とした。また、
Ａｌ量が少なすぎると、鋼板のＮを固定できないため、
焼鈍時に微細なＡｌＮが析出する。この微細なＡｌＮが
発生すると、焼鈍時の粒成長が不十分となり、高いｒmi
n が得られないので、ネックしわが発生してしまう。そ
こで本発明者らは、ネックしわが発生しないＡｌ量の下
限値を実験より求めた結果、Ａｌ量はＮ量に応じ、０．
０２３２ log（〔Ｎ％〕＋０．０１）＋０．１１６％以
上必要であることを知見した。Sol. If the Al content exceeds 0.100%, Al 2 O 3 -based inclusions increase and cracks occur during flange forming, so the upper limit was made 0.100%. Also,
If the amount of Al is too small, N of the steel sheet cannot be fixed,
Fine AlN precipitates during annealing. When this fine AlN is generated, the grain growth during annealing becomes insufficient, and a high r mi
Since n cannot be obtained, neck wrinkles occur. The inventors of the present invention have determined from experiments the lower limit of the amount of Al at which neck wrinkling does not occur.
It was found that 0232 log ([N%] + 0.01) + 0.116% or more was required.
【００１２】Ｎは０．００４０％超となると、熱延で高
温巻取りをして、ＡｌＮ析出を促進しても、熱延板に固
溶Ｎが多量に残存し、焼鈍時に微細なＡｌＮが析出して
しまう。そのため、焼鈍時の粒成長が不十分で、高いｒ
min 値が得られず、ネックしわが発生するので、上限を
０．００４０％とした。Ｔ．Ｏの含有量は、０．００７
０％超となると、スラブ表層付近に気泡が発生し、メッ
キ原板の表面キズが増え、良好な製品が得られなくなる
ので、上限を０．００７０％とした。When N exceeds 0.0040%, even if high-temperature winding is performed by hot rolling to promote AlN precipitation, a large amount of solid solution N remains in the hot-rolled sheet, and fine AlN is removed during annealing. Will precipitate. Therefore, the grain growth during annealing is insufficient, and a high r
Since the min value was not obtained and neck wrinkles occurred, the upper limit was made 0.0040%. T. The content of O is 0.007
If it exceeds 0%, air bubbles are generated in the vicinity of the surface layer of the slab, and the surface scratches of the plating original plate increase, so that a good product cannot be obtained. Therefore, the upper limit was made 0.0070%.
【００１３】上記のような成分組成の鋼は、次に述べる
製造条件と相まって、発明の目的が達成できる。以下に
製造工程について述べる。熱延時の加熱温度は特に規制
する必要がない。ただし、焼鈍時に微細なＡｌＮが析出
すると、焼鈍時の粒成長が阻害され、ｒmin 値が低下す
るので、できるだけ加熱時に鋼板のＮが固溶しない１２
００℃以下の加熱温度が望ましい。圧延温度は、８９０
℃未満では、熱延板粒径が小さく、Δｒが大きくなり、
ネック成形性が確保できないため、８９０℃を下限とし
た。また９５０℃を越えると、鋼板にスケールが発生す
るため、９５０℃以下とした。[0013] The steel having the above-described composition can achieve the object of the invention in combination with the production conditions described below. The manufacturing process will be described below. There is no particular need to regulate the heating temperature during hot rolling. However, if fine AlN precipitates during annealing, the grain growth during annealing is inhibited, and the rmin value decreases.
A heating temperature of 00 ° C or less is desirable. The rolling temperature is 890
If the temperature is lower than ℃, the hot-rolled sheet particle size is small and Δr is large
Since the neck formability cannot be ensured, the lower limit is 890 ° C. If the temperature exceeds 950 ° C., scale is generated on the steel sheet.
【００１４】熱延後の冷却速度は本発明の重要な因子で
ある。本発明者らは、熱延板の粒径を大きくするために
は、Ａｒ3 変態時の温度での冷速を小さくすることが重
要であることを発見した。冷却速度が５０℃／ｓ超で
は、熱延板の粒径が小さくなり、Δｒが大きくなる。そ
のため、高いｒmin 値が得られず、ネックしわが発生す
るので、上限を５０℃／ｓとした。The cooling rate after hot rolling is an important factor in the present invention. The present inventors have discovered that in order to increase the grain size of a hot-rolled sheet, it is important to reduce the cooling rate at the temperature during the Ar 3 transformation. When the cooling rate exceeds 50 ° C./s, the grain size of the hot-rolled sheet becomes small, and Δr becomes large. Therefore, a high r min value cannot be obtained and neck wrinkles occur. Therefore, the upper limit was set to 50 ° C./s.
【００１５】また、巻取温度も本発明の重要なポイント
である。巻取温度は６９０℃未満となれば、巻取り時
に、粗大なＡｌＮが十分析出できず、固溶Ｎが熱延板に
多量に残存する。このため、焼鈍時に微細なＡｌＮが析
出して粒成長が阻害され、ｒmi n 値が小さくなり、ネッ
クしわが発生するので、６９０℃を下限とした。また７
５０℃超となると、鋼板のスケールが発達し、酸洗時の
速度を落とさないとスケールが剥離できないので、７５
０℃を上限とした。熱延後は、酸洗、冷延工程を行い、
その後、連続焼鈍を行う。焼鈍時の焼鈍温度は、６９０
℃未満では、焼鈍時に十分粒成長せず、高いｒmin 値が
得られない。そのため、ネックしわが発生するので、６
９０℃を下限とした。また、７５０℃超では、セメンタ
イトが粗大化し、フランジ成形時にフランジ割れが発生
するため、７５０℃を上限とした。焼鈍後は１％以上１
０％以下の圧延を行う。１％未満では、カップ成形時に
Ｓｔ−Ｓｔが発生するため、下限を１％とした。また１
０％超では、硬質になりすぎ、ネック成形時にしわが発
生するので、上限を１０％とした。圧下後は、Ｓｎメッ
キによる表面皮膜を施す。[0015] The winding temperature is also an important point of the present invention. If the winding temperature is lower than 690 ° C., during winding, coarse AlN cannot be sufficiently precipitated, and a large amount of solid solution N remains on the hot-rolled sheet. Therefore, fine AlN precipitates during annealing is inhibited grain growth, r mi n value becomes small, because the neck wrinkles and the lower limit 690 ° C.. 7
When the temperature exceeds 50 ° C., the scale of the steel sheet develops, and the scale cannot be peeled unless the speed at the time of pickling is reduced.
The upper limit was 0 ° C. After hot rolling, perform pickling and cold rolling processes,
Thereafter, continuous annealing is performed. Annealing temperature during annealing is 690
If the temperature is lower than ℃, the grains do not grow sufficiently during annealing, and a high r min value cannot be obtained. As a result, neck wrinkles occur.
90 ° C was the lower limit. If the temperature exceeds 750 ° C., cementite becomes coarse and flange cracks occur during flange forming. 1% or more after annealing 1
Roll 0% or less. If it is less than 1%, St-St occurs at the time of cup molding, so the lower limit is set to 1%. Also one
If it exceeds 0%, it will be too hard and wrinkles will occur during neck molding, so the upper limit was made 10%. After the reduction, a surface coating by Sn plating is applied.
【００１６】[0016]
【実施例】以下に本発明の効果を実施例により説明す
る。表１に示す成分の２５０ｍｍ厚の鋼を、表２に示す
熱延条件で、２．５ｍｍの熱延鋼板を製造した。尚、表
２中の冷却パターンと冷却速度を図１に示す。冷却パタ
ーン２は冷速が一定となるように冷却を行った。表２中
にＡｒ3 変態時での冷速を示す。この熱延鋼板の組織を
観察し、Ｇ．Ｓ（結晶粒度）を調査した。次に酸洗し、
冷延率９０％で０．２５ｍｍまで冷延し、表２の条件で
連続焼鈍し、調質圧延を施し、表面処理原板を得た。表
２中の焼鈍条件でのＴ1 （℃）、Ｔ2（℃），ｔ
1 （秒）、ｔ2 （秒）の定義を図２に示す。この表面処
理原板のＧ．Ｓ、Ｌ、Ｄ、Ｃ方向のｒ値、ＹＰを実験よ
り求めた。次にこの表面処理原板を実験室のＤＩ成形機
を用いて、内径６６．１ｍｍ、ネック厚み１２５μｍ、
缶胴厚み８０μｍのＤＩ缶を各水準１００缶成形した。
このＤＩ缶を当社の１２段のダイネックマシンを用い
て、現在製缶メーカで計画されている内径６０．３ｍｍ
まで１２段でネック加工を行った。当社の１２段のダイ
ネックマシンとユーザーでのダイネックマシンとは、ネ
ックしわ発生状況に差がないことから、本実験機で１缶
もしわが発生しなかった表面処理原板を合格とした。
Ｇ．Ｓ、機械試験値、ネック成形試験結果を表３に示
す。EXAMPLES The effects of the present invention will be described below with reference to examples. Under the hot rolling conditions shown in Table 2, a 2.5 mm hot rolled steel sheet was manufactured from a 250 mm thick steel having the components shown in Table 1. The cooling patterns and cooling rates in Table 2 are shown in FIG. The cooling pattern 2 was cooled so that the cooling rate was constant. Table 2 shows the cooling speed during the Ar 3 transformation. Observing the structure of this hot-rolled steel sheet, S (crystal grain size) was investigated. Then pickle,
The sample was cold-rolled at a cold-rolling rate of 90% to 0.25 mm, continuously annealed under the conditions shown in Table 2, and subjected to temper rolling to obtain a surface-treated original sheet. T 1 (° C.), T 2 (° C.), t under the annealing conditions in Table 2
FIG. 2 shows the definitions of 1 (second) and t 2 (second). G. of this surface-treated original plate The r values in the S, L, D, and C directions and YP were determined by experiments. Next, using a laboratory DI molding machine, this surface-treated original plate was 66.1 mm in inner diameter and 125 μm in neck thickness.
DI cans having a can body thickness of 80 μm were molded into 100 cans of each level.
This DI can is manufactured using our 12-stage die-neck machine and has an inner diameter of 60.3 mm that is currently planned by the can manufacturer.
Neck processing was performed in 12 steps up to this. Since there is no difference in the state of neck wrinkling between our 12-stage die neck machine and the user's die neck machine, a surface-treated original sheet in which no wrinkles occurred in this experimental machine was accepted.
G. FIG. Table 3 shows S, mechanical test values, and neck forming test results.
【００１７】[0017]
【表１】 [Table 1]
【００１８】[0018]
【表２】 [Table 2]
【００１９】[0019]
【表３】 [Table 3]
【００２０】本発明内の符号１〜３は、１００缶ネック
成形を行ったが、１缶もしわが発生せず、合格した。ま
た、本発明外の符号４〜１３は、熱延板粒径、焼鈍板粒
径が小さいため、ｒ1 （ｒmin ）値が低くなり、ネック
しわがＬ方向近傍に発生し、不合格であった。符号８は
図１の冷却パターンで冷却し、ＦＴ直後は、１８℃／
ｓの緩冷却を行っているが、Ａｒ3 変態時の冷速は６０
℃／ｓと高くなっている。そのため、熱延板粒径が小さ
くなり、ｒmin 値（ｒL 値）が低くなり、ネックしわが
発生した。また符号１１は特にネックしわ発生率が高か
った。Ｓ．Ｐ率が１１％と高いため、ＹＰが高いのが原
因と推定される。In the present invention, the reference numerals 1 to 3 in the present invention were 100-neck-molded, but passed without any wrinkles. In addition, reference numerals 4 to 13 outside the present invention indicate that the r 1 (r min ) value is low due to the small grain size of the hot-rolled sheet and the grain size of the annealed sheet, and neck wrinkles occur in the vicinity of the L direction. there were. Reference numeral 8 denotes cooling by the cooling pattern of FIG.
s, but the cooling rate during Ar 3 transformation is 60
° C / s. Therefore, the grain size of the hot-rolled sheet was reduced, the r min value (r L value) was reduced, and neck wrinkling occurred. In addition, reference numeral 11 has a particularly high neck wrinkle occurrence rate. S. Since the P ratio is as high as 11%, it is presumed that YP is high.
【００２１】[0021]
【発明の効果】本発明のＤＩ缶用鋼板では、ネック成形
試験の結果、１００缶中１缶もしわが発生せず、製缶メ
ーカでの蓋の径小化に十分対応できるものである。According to the steel sheet for DI cans of the present invention, as a result of the neck forming test, no wrinkles occur in one out of every 100 cans, which can sufficiently cope with the reduction in the diameter of the lid in a can maker.
【図１】熱延後の鋼板の冷却パターンを示す図、FIG. 1 is a diagram showing a cooling pattern of a steel sheet after hot rolling,
【図２】冷延後の鋼板の連続焼鈍における焼鈍パターン
を示す図、FIG. 2 is a diagram showing an annealing pattern in continuous annealing of a steel sheet after cold rolling;
【図３】ＤＩ缶ネック加工の１つであるダイネック法の
概念図、FIG. 3 is a conceptual diagram of a die neck method which is one of DI can neck processing.
【図４】ＤＩ缶ネック加工の１つであるスピンネック法
の概念図、FIG. 4 is a conceptual diagram of a spin neck method which is one of DI can neck processing.
【図５】従来鋼での冷延率とΔｒとの関係を示す図、FIG. 5 is a diagram showing a relationship between a cold rolling reduction and Δr in a conventional steel;
【図６】従来鋼で、冷延率９０％の場合の板面各方向の
ｒ値を示す図である。FIG. 6 is a view showing r values in each direction of a sheet surface when a cold rolling rate is 90% in conventional steel.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 辻村 銑吉 福岡県北九州市戸畑区飛幡町１−１ 新 日本製鐵株式会社 八幡製鐵所内 (72)発明者 井上 満稔 東京都千代田区大手町二丁目６番３号 新日本製鐵株式会社内 (56)参考文献 特開 昭59−38336（ＪＰ，Ａ) 特開 昭63−223130（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 - 38/60 C21D 9/46 - 9/48 C21D 8/00 - 8/10 ────────────────────────────────────────────────── ─── Continuing on the front page (72) Inventor Tokichi Tsujimura 1-1 Hibata-cho, Tobata-ku, Kitakyushu-shi, Fukuoka New Nippon Steel Corporation Yawata Works (72) Inventor Mitsunori Inoue Otemachi, Chiyoda-ku, Tokyo 2-6-3 Nippon Steel Corporation (56) References JP-A-59-38336 (JP, A) JP-A-63-223130 (JP, A) (58) Fields investigated (Int. . 7, DB name) C22C 38/00 - 38/60 C21D 9/46 - 9/48 C21D 8/00 - 8/10
Claims (2)
１）＋０．１１６％以上０．１００％以下 Ｎ ：０．００４０％以下 Ｔ．Ｏ：０．００７０％以下 残部がＦｅ及び不可避的不純物からなる鋼より製造さ
れ、板面のＬ、Ｄ、Ｃ方向の各ｒ値の中で最も低いｒ値
が１．２以上であり、ネック成形時の耐しわ性に優れる
ことを特徴とするＤＩ缶用鋼板。C .: 0.02% or more and 0.03% or less Mn: 0.30% or less P: 0.025% or less S: 0.025% or less sol. Al: 0.0232 log ([N%] + 0.0
1) + 0.116% or more and 0.100% or less N: 0.0040% or less O: 0.0070% or less Manufactured from steel with the balance being Fe and unavoidable impurities, the lowest r value among the r values in the L, D, and C directions of the plate surface is 1.2 or more, and the neck is A steel sheet for DI cans characterized by having excellent wrinkle resistance during molding.
１）＋０．１１ ６％以上０．１００％以下 Ｎ ：０．００４０％以下 Ｔ．Ｏ：０．００７０％以下 残部がＦｅ及び不可避的不純物からなる鋼を連続鋳造
し、その後、８９０℃以上９５０℃以下で仕上圧延し、
Ａｒ3 変態時の冷却速度を５０℃／ｓ以下で冷却した
後、６９０℃以上７５０℃以下で巻取り、その後、酸
洗、冷延を行い、６９０℃以上７５０℃以下で連続焼鈍
し、１％以上１０％以下の圧延を行い、板面のＬ、Ｄ、
Ｃ方向の各ｒ値の中で最も低いｒ値が１．２以上であ
り、ネック成形時の耐しわ性に優れることを特徴とする
ＤＩ缶用鋼板の製造方法。2. In terms of% by weight, C: 0.02% or more and 0.03% or less Mn: 0.30% or less P: 0.025% or less S: 0.025% or less sol. Al: 0.0232 log ([N%] + 0.0
1) + 0.116% or more and 0.100% or less N: 0.0040% or less O: 0.0070% or less Continuous casting of steel whose balance is Fe and unavoidable impurities, and then finish rolling at 890 ° C or more and 950 ° C or less,
After cooling at a cooling rate of 50 ° C./s or less at the time of Ar 3 transformation, winding is performed at 690 ° C. or more and 750 ° C. or less, followed by pickling and cold rolling, and continuous annealing at 690 ° C. or more and 750 ° C. or less. % Or more and 10% or less is rolled, and L, D,
A method for producing a steel sheet for a DI can, characterized in that the lowest r value among the r values in the C direction is 1.2 or more, and the wrinkle resistance during neck forming is excellent.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34177995A JP3226775B2 (en) | 1995-12-27 | 1995-12-27 | Method for producing steel sheet for DI can with excellent necked-in workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34177995A JP3226775B2 (en) | 1995-12-27 | 1995-12-27 | Method for producing steel sheet for DI can with excellent necked-in workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH09176793A JPH09176793A (en) | 1997-07-08 |
| JP3226775B2 true JP3226775B2 (en) | 2001-11-05 |
Family
ID=18348700
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP34177995A Expired - Fee Related JP3226775B2 (en) | 1995-12-27 | 1995-12-27 | Method for producing steel sheet for DI can with excellent necked-in workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3226775B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5000467B2 (en) * | 2007-12-03 | 2012-08-15 | 新日本製鐵株式会社 | Steel plate for 3-piece can with high strength and excellent expandability and manufacturing method |
-
1995
- 1995-12-27 JP JP34177995A patent/JP3226775B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH09176793A (en) | 1997-07-08 |
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