JPH073334A - Production of steel sheet for low earing vessel - Google Patents

Production of steel sheet for low earing vessel

Info

Publication number
JPH073334A
JPH073334A JP14809493A JP14809493A JPH073334A JP H073334 A JPH073334 A JP H073334A JP 14809493 A JP14809493 A JP 14809493A JP 14809493 A JP14809493 A JP 14809493A JP H073334 A JPH073334 A JP H073334A
Authority
JP
Japan
Prior art keywords
less
cold rolling
rolling
hot
thickness
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
JP14809493A
Other languages
Japanese (ja)
Inventor
Takehide Senuma
武秀 瀬沼
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Priority to JP14809493A priority Critical patent/JPH073334A/en
Publication of JPH073334A publication Critical patent/JPH073334A/en
Withdrawn legal-status Critical Current

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  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

PURPOSE:To eliminate the causing of stretcher strains by subjecting dead soft steel having a specified compsn. to hot rolling, specifying the cooling rate, executing coiling, specifying the relationship between the sheet thickness after cold rolling and the sheet thickness of the hot rolled sheet and executing cold rolling. CONSTITUTION:Steel constituted of, by weight, <=0.003% C, <=0.2% Si, <=0.6% Mn, 0.01 to 0.1% Al and <=0.005% N, and the balance Fe is subjected to hot rolling at >=840 deg.C. The average cooling rate till coiling is regulated to 50 deg.C/sec, and it is coiled at deg.4O0 deg.C. After pickling, cold rolling is executed at 0.5 to 50% cold rolling ratio after recrystallization annealing so as to establish (th-tf)/ th<0.96 between the sheet thickness (th) of the hot rolled sheet and the final sheet thickness (tf) after the cold rolling, recrystallization annealing and subsequent cold rolling to regulate (tf) into 0.12 to 0.22mm. In this way, the plating original sheet for an extremely thin vessel small in earing can be obtd.

Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【産業上の利用分野】本発明はストレッチャーストレイ
ンが発生しない耐イヤリング性に優れた極薄容器用めっ
き原板の製造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 plating base plate for an ultrathin container, which is excellent in earring resistance and does not cause stretcher strain.

【0002】[0002]

【従来の技術】軽量化および省資源の観点から容器用原
板の極薄化が市場より要請されている。これに対応し、
材料供給メーカーでは従来の熱延−冷延−焼鈍−調質圧
延の工程で冷延率を高めることで極薄化を達成する努力
をしている。しかし、この場合は冷延後すでに板厚が極
めて薄いため、焼鈍を連続焼鈍で行なうと通板が難し
く、形状が悪化したり、場合によっては板破断が起こ
り、品質だけでなく操業上大きな問題になることがあ
る。この問題を回避する技術として、極低Cの鋼を冷延
後の板厚は極薄までは薄くせず、焼鈍後、従来の調質圧
延より大きな圧下率で冷延をすることにより、狙いの板
厚まで減厚しようとする技術が特公平1−52451号
公報で開示されている。
2. Description of the Related Art The market demands for an extremely thin original plate for a container from the viewpoint of weight saving and resource saving. Corresponding to this,
Material suppliers are making efforts to achieve ultra-thinness by increasing the cold rolling rate in the conventional hot rolling-cold rolling-annealing-temper rolling. However, in this case, since the plate thickness is already extremely thin after cold rolling, it is difficult to pass the plate when annealing is carried out by continuous annealing, the shape deteriorates, and in some cases plate breakage occurs, which is a major problem not only in quality but also in operation. May become. As a technique for avoiding this problem, the aim is to reduce the sheet thickness of ultra-low C steel after cold rolling to an extremely thin thickness, and after annealing, perform cold rolling at a larger reduction rate than conventional temper rolling. Japanese Patent Publication No. 1-52451 discloses a technique for reducing the plate thickness.

【0003】しかしこのようにして製造した鋼板は異方
性が大きくDI(drawing and ironing)加工をして製造
する2ピース缶においてDI加工後、開口部にイヤリン
グとよばれる缶胴の高さの不均一が顕著に起こり(イヤ
リングを定量的に表す指標としてイヤリング率がある
が、これは缶胴高さの最大値から最小値を引いて、最大
値で割った値に100を掛けた値である)、このイヤリ
ングが大きい場合、缶胴高さを揃えるためにトリミング
をすることになり、歩留りが低下するだけでなく、工程
が1つ増えるためコスト高になる。このイヤリングの問
題は、焼鈍後に行なう冷延率が大きい場合だけでなく、
焼鈍前の冷延の圧下率が大きいときも顕在化する傾向が
ある。この対策としては、熱延板の板厚を薄くして冷延
圧下率を下げることが考えられる。しかし、熱延板の薄
手化は仕上温度の低下や圧延荷重の増加を招き、品質お
よび通板の安定性に問題が生じるばかりでなく、表面積
が増えることによる酸洗コストの上昇をきたす。
However, the steel sheet produced in this manner has a large anisotropy, and in a two-piece can produced by DI (drawing and ironing) processing, after the DI processing, the opening has a height of the can body called earring. Non-uniformity occurs remarkably (Earring rate is an index that quantitatively expresses earrings. This is the value obtained by subtracting the minimum value from the maximum value of the barrel height and dividing by the maximum value, and then multiplying by 100. However, if the earrings are large, trimming is performed to make the can body heights uniform, which not only lowers the yield but also increases the cost because one process is added. The problem with this earring is not only when the cold rolling rate after annealing is large,
It also tends to become apparent when the cold rolling reduction before annealing is large. As a countermeasure against this, it is conceivable to reduce the cold rolling reduction by reducing the thickness of the hot rolled sheet. However, thinning of the hot-rolled sheet causes a decrease in finishing temperature and an increase in rolling load, which not only causes a problem in quality and stability of the threaded sheet but also causes an increase in pickling cost due to an increase in surface area.

【0004】[0004]

【発明が解決しようとする課題】本発明はこのような従
来の問題点を解消し、経済的な方法でイヤリングの小さ
い極薄容器用鋼板の製造方法を提供することを目的とす
る。
SUMMARY OF THE INVENTION It is an object of the present invention to solve the above problems of the prior art and to provide a method for manufacturing a steel sheet for ultra-thin containers with small earrings by an economical method.

【0005】[0005]

【課題を解決するための手段】本発明者は極薄容器用鋼
板のイヤリングに及ぼす製造条件の影響を詳細に検討
し、熱延板を極端に薄手化しなくても、極低炭素鋼を熱
延後、超低温巻取することにより著しく低減できること
を明らかにした。又、熱延後の冷速がイヤリングの生成
に大きな影響を及ぼすことも明らかにした。本発明はこ
れらの知見に基づくものであって、以下の構成を要旨と
する。すなわち、重量比でC :0.003%以下、
Si:0.2%以下、Mn:0.6%以下、
Al:0.005%以上、0.1%以下、N :0.0
05%以下と、さらに場合によってはTi:0.05%
以下、 Nb:0.05%以下、Zr:0.05%
以下、 B :0.005%以下のうち少なくとも
1種を含み、残部がFeおよび不可避的不純物からなる
鋼を840℃以上の温度で熱間圧延し、好ましくは仕上
圧延後、800℃までの平均冷速を30℃/sec以下と
し、圧延後、巻取までの平均冷速を50℃/secとし、4
00℃以下の温度で巻取、酸洗後、熱延板の板厚th と
冷間圧延、再結晶焼鈍、その後の冷間圧延を行なった最
終板厚tf の間に(th −tf )/th <0.96を成
り立たせ、再結晶焼鈍後の冷延率を0.5%以上、50
%以下とし、tf が0.22mm以下、0.12mm以上と
することを特徴とするストレッチャーストレインが発生
しない低イヤリング性に優れた極薄容器用鋼板の製造方
法である。
Means for Solving the Problems The present inventor has studied in detail the influence of the manufacturing conditions on the earrings of a steel sheet for ultra-thin containers, and has been able to heat ultra-low carbon steel without making the hot-rolled sheet extremely thin. After rolling, it was clarified that it can be significantly reduced by winding at ultra-low temperature. It was also clarified that the cold speed after hot rolling had a great influence on the formation of earrings. The present invention is based on these findings and has the following structures. That is, C: 0.003% or less by weight,
Si: 0.2% or less, Mn: 0.6% or less,
Al: 0.005% or more, 0.1% or less, N: 0.0
05% or less, and in some cases Ti: 0.05%
Below, Nb: 0.05% or less, Zr: 0.05%
Hereinafter, B: steel containing at least one of 0.005% or less and the balance of Fe and inevitable impurities is hot-rolled at a temperature of 840 ° C. or higher, preferably after finishing rolling, the average of up to 800 ° C. The cold speed is 30 ℃ / sec or less, and the average cold speed after rolling after rolling is 50 ℃ / sec.
After winding and pickling at a temperature of 00 ° C. or less, between the thickness t h of the hot rolled sheet and the final sheet thickness t f after cold rolling, recrystallization annealing and subsequent cold rolling (th −t f) / Th <0.96 is satisfied, and the cold rolling rate after recrystallization annealing is 0.5% or more, 50
% Or less and tf of 0.22 mm or less and 0.12 mm or more, which is a method for producing a steel sheet for ultra-thin containers excellent in low earring property without causing stretcher strain.

【0006】次に、本発明の限定条件を述べる。まず、
成分の限定条件について述べる。C量を0.003%以
下としたのは、いくつかの理由がある。まず、圧延後、
巻取までの平均冷速を50℃/secとし、400℃以下の
温度で巻取ることにより、イヤリングの低減を顕著に図
るにはC添加量の下限を0.003%にする必要があ
る。又、これ以上Cを添加するとストレッチャーストレ
インが発生することも根拠の1つである。Nは固溶状態
で鋼中に残るとストレッチャーストレイン発生の原因に
なるので、通常AlN,TiNなどのような析出物の状
態にするが、析出物の量が増えると加工性が劣化するの
で、Nの添加量自体を0.005%以下と限定した。
Next, the limiting conditions of the present invention will be described. First,
The conditions for limiting the components will be described. There are several reasons why the amount of C is set to 0.003% or less. First, after rolling,
By lowering the average cold speed until winding to 50 ° C./sec and winding at a temperature of 400 ° C. or lower, the lower limit of the amount of C added must be 0.003% in order to significantly reduce the earring. It is also one of the reasons that stretcher strain is generated when C is added further. If N remains in the steel in the form of a solid solution, it will cause stretcher strain to occur, so normally it is in the form of precipitates such as AlN and TiN, but if the amount of precipitates increases, the workability deteriorates. , N were limited to 0.005% or less.

【0007】Al量はNを窒化アルミとして固定するに
必要であり、最低で0.01%必要である。しかし、他
にTi,Nb,Zr,Bなどの窒化物形成元素が添加さ
れる場合は、Al脱酸を十分に実行することを主眼に置
き、0.005%以上の添加でよい。又、多量の添加は
コストアップになるだけでなく、加工性も劣化させるの
で、添加量の上限は0.1%とする。Si,Mnの添加
量をSi:0.2%以下、Mn:0.6%以下と限定し
たのは、これ以上これらの合金を添加すると、加工性の
劣化や耐食性を阻害する要因になる。又、Ti,Nb,
Zr,Bの添加は炭窒化物を形成し、固溶C,Nを排除
することにより加工性を向上するが、多量の添加はコス
ト高になるばかりか、逆に加工性を劣化するので、それ
ぞれの添加量の上限をTi:0.05%以下、Nb:
0.05%以下、Zr:0.05%以下、B:0.00
5%以下とした。
The amount of Al is necessary to fix N as aluminum nitride, and is required to be at least 0.01%. However, when a nitride-forming element such as Ti, Nb, Zr, or B is added in addition, 0.005% or more may be added with a focus on sufficiently performing Al deoxidation. Further, addition of a large amount not only increases the cost but also deteriorates workability, so the upper limit of the addition amount is 0.1%. The addition amounts of Si and Mn are limited to Si: 0.2% or less and Mn: 0.6% or less. If these alloys are further added, workability deteriorates and corrosion resistance is impaired. Also, Ti, Nb,
The addition of Zr and B forms carbonitrides and improves the workability by eliminating the solid solution C and N. However, addition of a large amount not only increases the cost but also deteriorates the workability. The upper limit of each addition amount is Ti: 0.05% or less, Nb:
0.05% or less, Zr: 0.05% or less, B: 0.00
It was set to 5% or less.

【0008】次に、製造条件の限定について述べる。熱
延仕上温度を840℃以上としたのは、本発明鋼の成分
では、これ以下の温度で仕上圧延をすると部分的あるい
は全部が仕上圧延時にフェライト組織になり、前者では
特性にバラツキが生じやすくなり、後者ではイヤリング
率が大きくなるためである。巻取温度を400℃以下と
したのは、図1,図2に示すように巻取温度がこの限定
条件を満足することにより、イヤリングが低減できるた
めである。この理由は必ずしも明らかではないが、巻取
温度を低温化することにより、固溶C,N量が増加する
か、生成する析出物が微細化するため、これが冷延、焼
鈍時に形成される集合組織に影響を与え、結果としてイ
ヤリングの低下を可能にしたものと考えられる。
Next, the limitation of manufacturing conditions will be described. The hot rolling finishing temperature is set to 840 ° C. or higher. With the composition of the steel of the present invention, if finish rolling is performed at a temperature lower than this, a part or all of the composition becomes a ferrite structure during finish rolling, and the former tends to cause variations in properties. This is because the earring rate increases in the latter case. The reason why the winding temperature is 400 ° C. or lower is that the earring can be reduced when the winding temperature satisfies this limiting condition as shown in FIGS. The reason for this is not clear, but by lowering the coiling temperature, the amount of solute C and N increases, or the precipitates that form become finer. Therefore, these are aggregates formed during cold rolling and annealing. It is thought to have affected the organization and consequently reduced the earrings.

【0009】又、仕上圧延後から400℃以下の巻取ま
での冷速を平均で50℃/sec以上としたのは、冷速がこ
れ以下だとイヤリングが顕著に小さくならないためであ
る。この原因も上記と同様に、平均冷速が50℃/sec以
下になると、固溶C,N量が減少し、生成する析出物も
十分に微細化しないためと推測される。一方、圧延後、
800℃までの平均冷速を30℃/sec以下と逆に上限を
限定したのは、この限定条件を満足することによりイヤ
リング率がより低下するためである。この原因は変態時
の冷速が小さいことにより生成するフェライト粒径が粗
大化し、それがイヤリングの低下に寄与したものと考え
られる。しかし、圧延後、800℃までの平均冷速を3
0℃/sec以下としただけでは、イヤリング率の低下は少
なく、圧延後、巻取までの平均冷速を50℃/secとし、
400℃以下の温度で巻取という条件が同時に満足され
ることにより始めてイヤリング率の顕著な減少が達成で
きる。
On the other hand, the reason why the cooling rate from finish rolling to winding at 400 ° C. or lower is 50 ° C./sec or more on average is that the earring does not become remarkably small when the cooling rate is lower than this. It is presumed that this is because, as in the above case, when the average cooling rate is 50 ° C./sec or less, the amount of solid-soluted C and N decreases, and the produced precipitate does not become sufficiently fine. On the other hand, after rolling,
The upper limit of the average cooling rate up to 800 ° C. of 30 ° C./sec or less is limited, because the earring rate is further reduced by satisfying this limiting condition. It is considered that this is because the grain size of ferrite generated due to the low cooling rate during transformation was coarsened, which contributed to the reduction of the earring. However, after rolling, the average cold speed up to 800 ° C is 3
If the rate is 0 ° C / sec or less, the earring rate will not decrease so much, and the average cooling speed after rolling after rolling is 50 ° C / sec.
Only when the conditions of winding at a temperature of 400 ° C. or less are satisfied at the same time, a remarkable reduction in the earring rate can be achieved.

【0010】熱延板の板厚th と最終板厚tf の間の関
係において、(th −tf )/th<0.96を限定条
件としたのは、図2に見られるようにこの条件範囲で本
発明鋼が比較鋼に比べて、優れた耐イヤリング性を示す
ためである。ここで、図2に見られるように、板厚減厚
を再結晶焼鈍前の冷延だけで達成しても、再結晶焼鈍に
冷延をして、再結晶焼鈍前の冷延の組み合わせで達成し
ても耐イヤリング性についてはほぼ同じ効果を示す。
In the relationship between the thickness t h of the hot-rolled sheet and the final sheet thickness t f, the limiting condition is (th −t f) / th <0.96, as shown in FIG. This is because the steel of the present invention exhibits excellent earring resistance as compared with the comparative steel. Here, as shown in FIG. 2, even if the sheet thickness reduction is achieved only by the cold rolling before the recrystallization annealing, the cold rolling is performed in the recrystallization annealing, and the combination of the cold rolling before the recrystallization annealing is performed. Even if it achieves, it shows almost the same effect on the earring resistance.

【0011】再結晶焼鈍後の冷延率を0.5%以上、5
0%以下と限定したのは、0.5%以下の冷延率では調
質効果が十分得られないためである。又、冷延率が50
%を超えるとDI加工時にボトルしわ、ネックしわ、フ
ランジ割れ、ティアーオフなど成形不良が発生する確率
が大きくなるためである。最終板厚tf を0.22mm以
下、0.12mm以上と限定したのは最終板厚tfが0.
22mm以上になると、本来の目標である軽量化、省資源
化が有効に達成できないためである。又、最終板厚tf
が0.12mm以下になると缶底の剛性が小さくなりす
ぎ、缶内圧により形状変化が顕著に起こるためである。
The cold rolling rate after recrystallization annealing is 0.5% or more, 5
The reason why it is limited to 0% or less is that the tempering effect cannot be sufficiently obtained at a cold rolling rate of 0.5% or less. The cold rolling rate is 50
This is because if it exceeds%, the probability of forming defects such as bottle wrinkles, neck wrinkles, flange cracks, tear-offs during DI processing increases. The reason why the final thickness tf is limited to 0.22 mm or less and 0.12 mm or more is that the final thickness tf is 0.
This is because if the thickness is 22 mm or more, the original goals of weight reduction and resource saving cannot be effectively achieved. Also, the final plate thickness tf
Is less than 0.12 mm, the rigidity of the bottom of the can becomes too small and the pressure inside the can remarkably changes the shape.

【0012】以上のように、本発明の基本構成は、極低
炭素鋼を極めて低い温度で巻取ることにより、従来は高
いイヤリング率を示す冷延率(再結晶焼鈍前後の冷延の
圧下率の総和)の範囲でイヤリング率を低減でき、極薄
の容器用鋼板を製造できると言うもので、今までにない
発想に基づいている。
As described above, according to the basic structure of the present invention, the cold rolling ratio showing the high earring ratio is conventionally obtained by winding the ultra low carbon steel at an extremely low temperature (the reduction ratio of the cold rolling before and after the recrystallization annealing). It is said that the earring rate can be reduced within the range of (1) and the ultra-thin steel sheet for containers can be manufactured, which is based on an unprecedented idea.

【0013】[0013]

【実施例】表1に本発明鋼と比較鋼の化学成分を示す。
又、表2には表1の材料を用いて、諸製造条件で製造し
た鋼板をDI加工したときのイヤリング率、ボトムしわ
の有無、ネックしわの有無、耐圧強度、ストレッチャー
ストレインの発生の有無を調べた結果を示す。ボトムし
わ、ネックしわ、ストレッチャーストレインの発生の有
無は肉眼による観察により判断した。耐圧強度は図3に
示す缶底形状で缶底が内圧により反転したときの圧力で
定義し、ここでは0.5MPa 以上で合格とした。
EXAMPLES Table 1 shows the chemical composition of the steel of the present invention and the comparative steel.
Table 2 shows the earring rate, the presence or absence of bottom creases, the presence or absence of neck creases, the proof pressure strength, and the presence or absence of stretcher strain when the steel sheets manufactured under various manufacturing conditions are DI processed using the materials of Table 1. The results of examination are shown below. The presence or absence of bottom wrinkles, neck wrinkles, and stretcher strain was judged by visual observation. The compressive strength is defined as the pressure when the can bottom is inverted by the internal pressure in the shape of the can bottom shown in FIG.

【0014】[0014]

【表1】 [Table 1]

【0015】[0015]

【表2】 [Table 2]

【0016】[0016]

【表3】 [Table 3]

【0017】[0017]

【表4】 [Table 4]

【0018】[0018]

【表5】 [Table 5]

【0019】本発明鋼である実験番号1,2,4,5,
8,9,11,14,16,17,18,21,22,
23,24,25はイヤリング率が低く、耐圧強度も満
足し、ボトムしわ、ネックしわ、ストレッチャーストレ
インなどの発生もなく、優れた缶成形成を示した。熱延
仕上温度が本発明の範囲以下であった実験番号3は熱延
板の集合組織が異なるためか、イヤリング率が高かっ
た。巻取温度が本発明の範囲を超えた実験番号6,10
は共に高いイヤリング率を示した。又、仕上圧延後から
巻取までの平均冷速が本発明の範囲以下であった実験番
号7も高いイヤリング率を示した。(th −tf )/t
h の比が本発明の範囲を超えた実験番号12も高いイヤ
リング率を示した。再結晶焼鈍後に60%の冷延を行な
った実験番号13では、加工硬化が大きかったためか缶
成形時にしわが観察された。又、最終板厚が0.11mm
と本発明の範囲より薄い実験番号15ではボトムしわの
発生のほかに、耐圧強度が合格の水準に達しなかった。
C,Nが本発明の範囲より多く添加された実験番号1
9,20,26ではストレッチャーストレインが発生し
た。特に、C量の多かった実験番号26ではしわの発生
も観察された。
Experiment Nos. 1, 2, 4, 5, which are steels of the present invention
8, 9, 11, 14, 16, 17, 18, 21, 22, 22
Nos. 23, 24, and 25 had a low earring rate, satisfied the pressure resistance, and did not generate bottom wrinkles, neck wrinkles, stretcher strains, etc., and showed excellent canned formation. In Experiment No. 3 in which the hot rolling finishing temperature was below the range of the present invention, the earring rate was high probably because the texture of the hot rolled sheet was different. Experiment numbers 6 and 10 in which the winding temperature exceeded the range of the present invention
Both showed high earring rates. Further, Experiment No. 7 in which the average cold speed from finish rolling to winding was below the range of the present invention also showed a high earring rate. (Th-tf) / t
Experiment number 12, in which the h ratio exceeded the range of the present invention, also showed a high earring rate. In Experiment No. 13 in which 60% cold rolling was performed after recrystallization annealing, wrinkles were observed during can forming, probably because work hardening was large. Also, the final plate thickness is 0.11 mm
In Experiment No. 15 thinner than the range of the present invention, in addition to the occurrence of bottom wrinkles, the pressure resistance did not reach the acceptable level.
Experiment No. 1 in which C and N were added in excess of the range of the present invention
Stretcher strain occurred on 9, 20, and 26. In particular, wrinkles were also observed in Experiment No. 26, in which the amount of C was large.

【0020】[0020]

【発明の効果】以上のように、本発明は、極薄容器用鋼
板の製造において従来問題とされていたイヤリングを低
減できる新技術を提供するもので、その工業的意味は大
きい。
INDUSTRIAL APPLICABILITY As described above, the present invention provides a new technique capable of reducing earrings, which has been a problem in the production of steel sheets for ultrathin containers, and has a great industrial significance.

【図面の簡単な説明】[Brief description of drawings]

【図1】イヤリング率に及ぼす巻取温度の影響を示す。FIG. 1 shows the effect of winding temperature on the earring rate.

【図2】イヤリング率に及ぼす(熱延板板厚−最終板
厚)と熱延板板厚の比の関係と巻取温度をパラメータに
示す。
FIG. 2 shows the relationship between the ratio of (hot-rolled sheet thickness-final sheet thickness) and hot-rolled sheet thickness that affect the earring rate and the winding temperature as parameters.

【図3】耐圧強度を測定した缶の底の形状を示す。FIG. 3 shows the shape of the bottom of a can whose pressure resistance is measured.

Claims (3)

【特許請求の範囲】[Claims] 【請求項1】 重量比で C :0.003%以下、 Si:0.2%以下、 Mn:0.6%以下、 Al:0.01%以上、0.1%以下、 N :0.005%以下を含み、残部がFeおよび不可
避的不純物からなる鋼を840℃以上の温度で熱間圧延
し、圧延後、巻取までの平均冷速を50℃/secとし、4
00℃以下の温度で巻取、酸洗後、熱延板の板厚th と
冷間圧延、再結晶焼鈍、その後の冷間圧延を行なった最
終板厚tf の間に(th −tf )/th <0.96を成
り立たせ、再結晶焼鈍後の冷延率を0.5%以上、50
%以下とし、tf が0.22mm以下、0.12mm以上と
することを特徴とするストレッチャーストレインが発生
しない低イヤリング容器用鋼板の製造方法。
1. By weight ratio, C: 0.003% or less, Si: 0.2% or less, Mn: 0.6% or less, Al: 0.01% or more, 0.1% or less, N: 0. Steel containing 005% or less and the balance of Fe and unavoidable impurities is hot-rolled at a temperature of 840 ° C. or higher, and the average cold speed until rolling after rolling is 50 ° C./sec.
After winding and pickling at a temperature of 00 ° C. or less, between the thickness t h of the hot rolled sheet and the final sheet thickness t f after cold rolling, recrystallization annealing and subsequent cold rolling (th −t f) / Th <0.96 is satisfied, and the cold rolling rate after recrystallization annealing is 0.5% or more, 50
% Or less, and tf is 0.22 mm or less and 0.12 mm or more, a method for producing a steel plate for a low earring container free from stretcher strain.
【請求項2】 重量比で C :0.003%以下、 Si:0.2%以下、 Mn:0.6%以下、 Al:0.005%以上、0.1%以下、 N :0.005%以下と、さらに Ti:0.05%以下、 Nb:0.05%以下、 Zr:0.05%以下、 B :0.005%以下のうち少なくとも1種を含み、
残部がFeおよび不可避的不純物からなる鋼を840℃
以上の温度で熱間圧延し、圧延後、巻取までの平均冷速
を50℃/secとし、400℃以下の温度で巻取、酸洗
後、熱延板の板厚tf と冷間圧延、再結晶焼鈍、その後
の冷間圧延を行なった最終板厚tf の間に(th −tf
)/th <0.96を成り立たせ、再結晶焼鈍後の冷
延率を0.5%以上、50%以下とし、tf が0.22
mm以下、0.12mm以上とすることを特徴とするストレ
ッチャーストレインが発生しない低イヤリング容器用鋼
板の製造方法。
2. By weight ratio, C: 0.003% or less, Si: 0.2% or less, Mn: 0.6% or less, Al: 0.005% or more, 0.1% or less, N: 0. 005% or less, further Ti: 0.05% or less, Nb: 0.05% or less, Zr: 0.05% or less, B: 0.005% or less, at least one kind is included,
Steel with balance of Fe and inevitable impurities at 840 ° C
After hot rolling at the above temperature, the average cold speed after rolling to winding is 50 ° C / sec, winding at a temperature of 400 ° C or less, pickling, hot rolled sheet thickness tf and cold rolling , Recrystallization annealing, and then cold rolling, during the final plate thickness tf (th-tf
) / Th <0.96, the cold rolling rate after recrystallization annealing is 0.5% or more and 50% or less, and tf is 0.22.
A method for producing a steel plate for a low earring container, in which stretcher strain does not occur, wherein the steel sheet has a thickness of 0.1 mm or less and 0.12 mm or more.
【請求項3】 仕上熱延後から800℃までの平均冷却
速度を30℃/sec以下とすることを特徴とする請求項1
又は2記載のストレッチャーストレインが発生しない低
イヤリング容器用鋼板の製造方法。
3. The average cooling rate after finishing hot rolling to 800 ° C. is 30 ° C./sec or less.
Alternatively, the method for producing a steel plate for a low earring container, according to 2, wherein the stretcher strain does not occur.
JP14809493A 1993-06-18 1993-06-18 Production of steel sheet for low earing vessel Withdrawn JPH073334A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP14809493A JPH073334A (en) 1993-06-18 1993-06-18 Production of steel sheet for low earing vessel

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP14809493A JPH073334A (en) 1993-06-18 1993-06-18 Production of steel sheet for low earing vessel

Publications (1)

Publication Number Publication Date
JPH073334A true JPH073334A (en) 1995-01-06

Family

ID=15445111

Family Applications (1)

Application Number Title Priority Date Filing Date
JP14809493A Withdrawn JPH073334A (en) 1993-06-18 1993-06-18 Production of steel sheet for low earing vessel

Country Status (1)

Country Link
JP (1) JPH073334A (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2700731A1 (en) * 2011-04-21 2014-02-26 JFE Steel Corporation Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2700731A1 (en) * 2011-04-21 2014-02-26 JFE Steel Corporation Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same
EP2700731A4 (en) * 2011-04-21 2015-04-08 Jfe Steel Corp Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same
US10174393B2 (en) 2011-04-21 2019-01-08 Jfe Steel Corporation Steel sheet for can with high barrel-part buckling strength under external pressure and with excellent formability and excellent surface properties after forming, and process for producing same

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