JPH10168544A - Cold rolled steel sheet excellent in blanking property and its production - Google Patents
Cold rolled steel sheet excellent in blanking property and its productionInfo
- Publication number
- JPH10168544A JPH10168544A JP8329649A JP32964996A JPH10168544A JP H10168544 A JPH10168544 A JP H10168544A JP 8329649 A JP8329649 A JP 8329649A JP 32964996 A JP32964996 A JP 32964996A JP H10168544 A JPH10168544 A JP H10168544A
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- steel sheet
- less
- cold
- rolled steel
- steel
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- 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.)
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、各種電機部品など
穴あけ加工が多数なされる冷延鋼板において、特に良好
な打ち抜き性を有する冷延鋼板及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 cold-rolled steel sheet having a particularly good punching property and a method for producing the same, particularly in a cold-rolled steel sheet in which a large number of holes are drilled such as various electric parts.
【０００２】[0002]
【従来の技術】極低炭素鋼にＴｉ，Ｎｂなどの炭窒化物
形成元素を添加したＩＦ鋼（Ｉｎｔｅｒｓｔｉｔｉａｌ
Ｆｒｅｅ Ｓｔｅｅｌ）は、優れたプレス成形性、深
絞り性を有するため、自動車用材料ならびに電機部品用
材料等に多く用いられている。特に、電機産業におい
て、用いられる冷延鋼板では、ねじ穴のための穴あけ加
工が多数なされる場合が多い。この際、穴あけは打ち抜
きによる場合がほとんどで、打ち抜きにより発生するバ
リが、電機機器における導電の問題やねじ切り作業上の
問題につながる場合がある。2. Description of the Related Art IF steel (Interstitial) in which a carbonitride forming element such as Ti or Nb is added to an ultra-low carbon steel.
Free Steel) has excellent press formability and deep drawability, and is therefore often used as a material for automobiles and a material for electric parts. Particularly, in the electrical industry, a cold-rolled steel sheet used is often subjected to a large number of drillings for screw holes. At this time, punching is almost always performed by punching, and burrs generated by punching may lead to problems in conductivity in electrical equipment and problems in threading work.
【０００３】このような背景の下、冷延鋼板の打ち抜き
性改善方法として、特開平１−２３０７４８号公報のＳ
量の増加による鋼中のＭｎＳを利用する方法、特開平６
−７３４５７号公報のＳ量の増加によるＴｉＳを利用す
る方法、及び特開平８−７３９９２号公報のＮ量の増加
により鋼中に生成するＴｉＮを利用する方法、さらに鋼
板を高強度化する方法等が開示されている。Under such a background, as a method for improving the punchability of a cold-rolled steel sheet, Japanese Patent Application Laid-Open No.
Utilizing MnS in steel by increasing the amount
No. 73457, a method using TiS by increasing the amount of S, Japanese Patent Application Laid-Open No. 8-73692, a method using TiN generated in steel by increasing the amount of N, and a method of increasing the strength of a steel sheet. Is disclosed.
【０００４】[0004]
【発明が解決しようとする課題】しかし、上記特開平１
−２３０７４８号公報、特開平６−７３４５７号公報、
及び特開平８−７３９９２号公報の技術はいずれの場合
もＳ，Ｎ量を増加することになり、鋼板の成形性は必ず
しも良好とはならない。また、鋼板の高強度化の対策に
ついては、こと電機部品用材料においては、成形後の形
状が重要であり、スプリングバックが問題となる。一
方、例えば、特開平３−２７７７３９号公報のように、
冷延鋼板の表層と中央部の成分を異成分とすることで、
表層部のみ硬化させて耐バリ性を向上させる技術も見ら
れるが、０．７〜１ｍｍ程度の板厚において鋼成分を異
ならせることは現在の薄鋼板製造技術上、現実的とは言
えず、コストアップにつながることは容易に想定され
る。However, Japanese Patent Application Laid-Open No.
-230748, JP-A-6-73457,
In each case, the techniques disclosed in Japanese Patent Application Laid-Open No. H8-73992 increase the amounts of S and N, and the formability of the steel sheet is not always good. As for measures for increasing the strength of a steel sheet, the shape after forming is important for a material for electric parts, and springback is a problem. On the other hand, for example, as disclosed in JP-A-3-27739,
By making the components of the surface layer and the central part of the cold-rolled steel sheet different components,
There is also a technology to improve the burr resistance by hardening only the surface layer, but it is not realistic in the current thin steel plate manufacturing technology to vary the steel composition at a thickness of about 0.7 to 1 mm. It is easily assumed that the cost will increase.
【０００５】本発明の目的は、このような事情を考慮し
てなされたものであり、Ｔｉ−ＩＦ鋼の打ち抜き性を向
上させるミクロ組織に制御すること、及び該組織を得る
ための製造条件を明確にすることにより、打ち抜き性の
良好な冷延鋼板およびその製造方法を提供することにあ
る。The object of the present invention has been made in view of such circumstances, and it is necessary to control the microstructure to improve the punchability of Ti-IF steel and to adjust the manufacturing conditions for obtaining the microstructure. It is an object of the present invention to provide a cold-rolled steel sheet having good punching properties and a method for manufacturing the same.
【０００６】[0006]
【課題を解決するための手段】前記課題を解決し目的を
達成するために、本発明は以下に示す手段を用いてい
る。 （１）本発明の冷延鋼板は、重量％で、Ｃ：０．００３
％以下と、Ｓｉ：０．３％以下と、Ｍｎ：０．０５〜
０．５％と、Ｐ：０．０３％以下と、Ｓ：０．００３〜
０．０１５％と、Ｓｏｌ．Ａｌ：０．０３〜０．０６％
と、Ｔｉ：０．０２〜０．０８％と、Ｎ：０．００３％
以下とを含有し、鋼板表面から板厚１５％以内の表層部
と鋼板表面から板厚１５％以内を除いた板厚中心部（以
下、この部分を板厚中心部と称する。）における平均フ
ェライト粒径をそれぞれｄｓ、ｄｂとするとき、ｄｓ／
ｄｂが０．９５以下であることを特徴とする打ち抜き性
に優れる冷延鋼板である。 （２）本発明の冷延鋼板は、さらに、重量％で、Ｂ：
０．０００２〜０．００１５％を含有することを特徴と
する上記（１）に記載の打ち抜き性に優れる冷延鋼板で
ある。In order to solve the above problems and achieve the object, the present invention uses the following means. (1) The cold-rolled steel sheet of the present invention has a C: 0.003 by weight%.
% Or less, Si: 0.3% or less, and Mn: 0.05 to
0.5%, P: 0.03% or less, S: 0.003 to
0.015% and Sol. Al: 0.03 to 0.06%
And Ti: 0.02 to 0.08% and N: 0.003%
The average ferrite in the central portion of the sheet thickness excluding the surface layer portion having a thickness of 15% or less from the surface of the steel sheet and the thickness of 15% or less from the surface of the steel sheet (hereinafter, this portion is referred to as the central portion of the sheet thickness). When the particle diameters are ds and db, respectively, ds /
It is a cold rolled steel sheet having excellent punchability, wherein db is 0.95 or less. (2) The cold-rolled steel sheet of the present invention further comprises B:
The cold rolled steel sheet having excellent punchability as described in (1) above, which contains 0.0002 to 0.0015%.
【０００７】（３）本発明の冷延鋼板は、さらに、重量
％で、Ｎｂ：０．００５〜０．０３％を含有することを
特徴とする上記（１）または（２）に記載の打ち抜き性
に優れる冷延鋼板である。(3) The blank according to the above (1) or (2), wherein the cold-rolled steel sheet of the present invention further contains 0.005 to 0.03% by weight of Nb. This is a cold rolled steel sheet with excellent heat resistance.
【０００８】（４）本発明の冷延鋼板の製造方法は、上
記（１）に記載の冷延鋼板を製造する方法において、連
続鋳造した鋼を１０００〜１２００℃に加熱する工程
と、加熱された鋼をＡｒ3 点以下の温度域で最終粗圧延
を行う工程と、粗圧延された鋼をＡｒ3 点以上（Ａｒ3
＋１００）℃未満の温度域まで加熱速度５℃／ｓ以上で
再加熱し、Ａｒ3 点以上で仕上げ圧延を行い、巻取る工
程と、巻取った熱延鋼板を冷延し、再結晶温度〜８５０
℃で焼鈍し、１．５％以下の調圧率で調質圧延を行う工
程と、を備えたことを特徴とする打ち抜き性に優れる冷
延鋼板の製造方法である。 （５）本発明の冷延鋼板の製造方法は、鋼板が、さら
に、重量％で、Ｂ：０．０００２〜０．００１５％を含
有していることを特徴とする上記（４）に記載の打ち抜
き性に優れる冷延鋼板の製造方法である。(4) The method for producing a cold-rolled steel sheet according to the present invention described in (1) above comprises the steps of: heating the continuously cast steel to 1000 to 1200 ° C .; and a step of performing a final rough rolling at a temperature range Ar 3 point of the steel, the rough rolling steel Ar 3 or more points (Ar 3
+100) Reheating at a heating rate of 5 ° C / s or more to a temperature range of less than 0 ° C, performing finish rolling at 3 points or more of Ar, winding, and cold rolling the hot-rolled steel sheet, and recrystallization temperature to 850
A step of annealing at ℃ and subjecting to temper rolling at a pressure regulation rate of 1.5% or less. (5) The method for producing a cold-rolled steel sheet according to the present invention, wherein the steel sheet further contains B: 0.0002 to 0.0015% by weight. This is a method for producing a cold-rolled steel sheet having excellent punchability.
【０００９】（６）本発明の冷延鋼板の製造方法は、鋼
板が、さらに、重量％で、Ｎｂ：０．００５〜０．０３
％を含有していることを特徴とする上記（４）または
（５）に記載の打ち抜き性に優れる冷延鋼板の製造方法
である。(6) In the method for producing a cold-rolled steel sheet according to the present invention, the steel sheet may further comprise Nb: 0.005 to 0.03 by weight%.
%, Wherein the cold-rolled steel sheet is excellent in punchability as described in the above item (4) or (5).
【００１０】[0010]
【発明の実施の形態】本発明者は、Ｔｉ−ＩＦ鋼の打ち
抜き性を向上させるミクロ組織に制御すること、及び該
組織を得るための製造条件を明確にすることにより、打
ち抜き性の良好な冷延鋼板を得るために、冷延鋼板の鋼
成分、及び金属組織すなわちフェライト粒径と打ち抜き
性との関係について、鋭意研究を重ねた。その結果、鋼
板表面から板厚１５％以内の表層部と板厚中心部におけ
る平均フェライト粒径をそれぞれｄｓ、ｄｂとすると
き、ｄｓ／ｄｂを０．９５以下という限られた範囲に制
御することが、打ち抜き性の向上に有効であるという知
見を得た。また、ＢあるいはＮｂを微量添加することに
より、打ち抜き性がさらに向上するという知見も得た。
以上の知見に基づき、本発明者は、極低炭素Ｔｉ−ＩＦ
鋼をベースとし、さらにＢあるいはＮｂを微量添加し、
熱延条件、冷延後の焼鈍条件及び調質圧延条件を調整し
て、鋼板の金属組織を上記の範囲に制御するようにし
て、打ち抜き性に優れる本発明の冷延鋼板及びその製造
方法を見出し、本発明を完成した。BEST MODE FOR CARRYING OUT THE INVENTION The present inventor controls the microstructure to improve the punching property of Ti-IF steel and clarifies the manufacturing conditions for obtaining the structure, thereby improving the punching property. In order to obtain a cold-rolled steel sheet, intensive studies were conducted on the steel composition and the metal structure of the cold-rolled steel sheet, that is, the relationship between the ferrite grain size and the punchability. As a result, when the average ferrite grain size in the surface layer portion and the central portion of the sheet thickness within 15% of the sheet thickness from the steel sheet surface is ds and db, respectively, ds / db is controlled to a limited range of 0.95 or less. Has been found to be effective in improving the punching performance. It was also found that the addition of a small amount of B or Nb further improves the punching property.
Based on the above findings, the present inventor has proposed an ultra-low carbon Ti-IF
Based on steel, further added a small amount of B or Nb,
By adjusting the hot rolling conditions, the annealing conditions after cold rolling and the temper rolling conditions to control the metallographic structure of the steel sheet within the above range, the cold rolled steel sheet of the present invention having excellent punchability and the method for producing the same are provided. Heading, the present invention has been completed.
【００１１】すなわち、本発明は、鋼組成、金属組織及
び製造条件を下記範囲に限定することにより、打ち抜き
性に優れる冷延鋼板を得ることができる。以下に本発明
の成分添加理由、成分限定理由、金属組織の限定理由及
び製造条件の限定理由について説明する。That is, according to the present invention, a cold-rolled steel sheet having excellent punching properties can be obtained by limiting the steel composition, the metal structure and the manufacturing conditions to the following ranges. The reasons for adding the components, the reasons for limiting the components, the reasons for limiting the metal structure, and the reasons for limiting the manufacturing conditions of the present invention will be described below.
【００１２】（１）成分組成範囲 Ｃ：０．００３％以下 Ｃは鋼板の成形性を確保するために少ないほうが望まし
い。実用上、本発明のの効果を損なわない量として、上
限は０．００３％である。成形性向上に対し、望ましく
はその上限は０．００２５％である。(1) Component composition range C: 0.003% or less C is preferably as small as possible to secure the formability of the steel sheet. In practical terms, the upper limit is 0.003% as an amount that does not impair the effects of the present invention. Desirably, the upper limit is 0.0025% for improving the moldability.
【００１３】Ｓｉ：０．３％以下 Ｓｉは固溶強化元素であるため、過度に添加すると鋼板
の強度が上昇し、加工性が劣化する。このため、上限は
０．３％であるが、好ましくは０．１５％以下である。Si: 0.3% or less Since Si is a solid solution strengthening element, if added excessively, the strength of the steel sheet increases and the workability deteriorates. For this reason, the upper limit is 0.3%, but preferably 0.15% or less.
【００１４】Ｍｎ：０．０５〜０．５％ ＭｎもＳｉと同様、固溶強化元素であり、０．５％を超
えて添加すると鋼板の強度上昇に伴う材質の劣化が生じ
る。従って、上限は０．５％である。好ましくは０．２
％以下である。下限値については、０．０５％を下回る
ような鋼組成とする場合には、製鋼上のコストアップに
つながるため、０．０５％である。Mn: 0.05 to 0.5% Mn is a solid solution strengthening element like Si, and if it is added in excess of 0.5%, the material is deteriorated due to an increase in the strength of the steel sheet. Therefore, the upper limit is 0.5%. Preferably 0.2
% Or less. The lower limit is 0.05% because a steel composition lower than 0.05% leads to an increase in steelmaking cost.
【００１５】Ｐ：０．０３％以下 ＰはＳｉ，Ｍｎと同様、固溶強化元素であり、少量で鋼
板の強度を上昇させる。Ｐ量の上昇により、打ち抜き性
は改善されるものの、高強度化により成形性が劣化する
ため、上限は０．０３％であり、望ましくは０．０１５
％以下である。P: not more than 0.03% P, like Si and Mn, is a solid solution strengthening element and increases the strength of the steel sheet by a small amount. Although the punching property is improved by increasing the amount of P, the formability is deteriorated by the increase in strength. Therefore, the upper limit is 0.03%, and preferably 0.015%.
% Or less.
【００１６】Ｓ：０．００３〜０．０１５％ Ｓは低減するのが望ましいが、０．００３％を下回る
と、熱延スケールの剥離性が低下する。一方、０．０１
５％を超えて含有すると、延性を低下させるため０．０
０３〜０．０１５％である。S: 0.003 to 0.015% S is desirably reduced, but if it is less than 0.003%, the releasability of the hot-rolled scale decreases. On the other hand, 0.01
If the content exceeds 5%, the ductility is reduced.
03-0.015%.
【００１７】Ｓｏｌ．Ａｌ：０．０３〜０．０６％ Ａｌは脱酸に必要であり、その下限は０．０３％であ
る。また、多量に添加するとコストが上昇するため、
０．０６％以下である。好ましくは、０．０５％以下で
ある。Sol. Al: 0.03 to 0.06% Al is necessary for deoxidation, and the lower limit is 0.03%. Also, adding a large amount increases the cost,
0.06% or less. Preferably, it is 0.05% or less.
【００１８】Ｎ：０．００３％以下 ＮはＩＦ鋼の高い成形性を確保するために、低いほうが
望ましく、その上限は０．００３％である。望ましくは
０．００２５％以下である。 Ｔｉ：０．０２〜０．０８％ Ｔｉは強力な炭窒化物形成元素であり、極低炭素鋼に添
加することにより、鋼板の成形性は向上する。Ｔｉ−Ｉ
Ｆ鋼特有の高い深絞り性を得るには、最低０．０２％は
必要であり、この値が下限である。一方、０．０８％を
超えて添加するとスラブコストが上昇するだけでなく、
冷延鋼板の表面性状が劣化しやすくなるので上限は０．
０８％である。N: 0.003% or less N is preferably as low as possible in order to ensure high formability of the IF steel, and the upper limit is 0.003%. Desirably, it is 0.0025% or less. Ti: 0.02 to 0.08% Ti is a strong carbonitride forming element, and when added to extremely low carbon steel, the formability of the steel sheet is improved. Ti-I
In order to obtain the high deep drawability unique to F steel, at least 0.02% is necessary, and this value is the lower limit. On the other hand, adding more than 0.08% not only increases the slab cost,
Since the surface properties of the cold-rolled steel sheet are likely to deteriorate, the upper limit is set to 0.
08%.
【００１９】Ｂ：０．０００２〜０．００１５％ ＢはＴｉと複合添加されることにより、打ち抜き性を向
上させる。また、副次的には耐縦割れ性を向上させるこ
とも可能であり、Ｔｉ−ＩＦ鋼の不可避的な耐二次加工
脆性の向上が可能となる。０．０００２％以上で、Ｂに
よる更なる鋼板表層の細粒化効果が認められるため、下
限値は０．０００２％である。また、０．００１５％を
超えて含有させると、鋼板自体の深絞り性が劣化しやす
くなるので、上限値は０．００１５％である。 Ｎｂ：０．００５〜０．０３％ ＮｂもＴｉと同様炭窒化物形成元素であり、極低炭素鋼
に添加することにより、鋼板の成形性は向上すると共
に、Ｎｂによる鋼板表層の細粒化効果が期待されるた
め、Ｔｉ−ＩＦ鋼に比べ打ち抜き性を更に向上させる。
Ｔｉと複合添加する場合、過剰なＮｂ添加はスラブコス
トの上昇のみならず、延性の劣化につながるため、上限
値は０．０３％である。また、０．００５％を下回る添
加では、Ｎｂによる打ち抜き性の向上効果が得られなく
なるため、下限値は０．００５％である。B: 0.0002 to 0.0015% B is added in combination with Ti to improve punchability. It is also possible to improve the vertical cracking resistance as a secondary effect, and it is possible to improve the inevitable secondary working brittleness of Ti-IF steel. When the content is 0.0002% or more, the further effect of B on refining the surface layer of the steel sheet is recognized, so the lower limit is 0.0002%. Further, if the content exceeds 0.0015%, the deep drawability of the steel sheet itself is likely to deteriorate, so the upper limit is 0.0015%. Nb: 0.005 to 0.03% Nb is also a carbonitride forming element like Ti, and when added to ultra-low carbon steel, the formability of the steel sheet is improved and the surface layer of the steel sheet is refined by Nb. Since the effect is expected, the punchability is further improved as compared with Ti-IF steel.
In the case where Ti is added in combination with Ti, excessive addition of Nb not only increases slab cost but also leads to deterioration of ductility, so the upper limit is 0.03%. On the other hand, if the addition is less than 0.005%, the effect of improving the punching property by Nb cannot be obtained, so the lower limit is 0.005%.
【００２０】（２）金属組織 本発明の金属組織は、鋼板表面から板厚１５％以内の表
層部と板厚中心部における平均フェライト粒径をそれぞ
れｄｓ、ｄｂとするとき、ｄｓ／ｄｂが０．９５以下で
ある。ｄｓ／ｄｂが０．９５を超えると、良好な打ち抜
き特性が得られない。(2) Metal Structure The metal structure of the present invention is such that when the average ferrite grain size in the surface layer portion and the center portion of the sheet thickness within 15% of the sheet thickness from the surface of the steel sheet is ds and db, respectively, ds / db is 0. .95 or less. If ds / db exceeds 0.95, good punching characteristics cannot be obtained.
【００２１】本発明においては、冷延鋼板の打ち抜き性
を改善するための焼鈍後の鋼板のミクロ組織として、鋼
板表層部のＴｉＣの析出形態として微細析出させること
及び表層近傍のフェライト組織を内層より微細組織にす
ることで、材質的に表層部を内層より硬化させることに
より、打ち抜き性を向上させようとするものである。In the present invention, as the microstructure of the annealed steel sheet for improving the punchability of the cold-rolled steel sheet, fine precipitation is performed as a precipitation form of TiC on the surface layer of the steel sheet, and the ferrite structure near the surface layer is removed from the inner layer. By forming a fine structure, the surface layer is hardened from the inner layer in terms of the material, thereby improving the punching property.
【００２２】従って、板厚の１５％以内の表層部と板厚
中心部における平均フェライト粒径をそれぞれｄｓ、ｄ
ｂとするとき、ｄｓ／ｄｂが０．９５以下であることが
重要である。ｄｓ／ｄｂの下限値については、特に規定
されるものではないが、現実的に本発明によって得られ
るｄｓ／ｄｂの最小値は０．４前後の値である。Therefore, the average ferrite grain size in the surface layer portion and the center portion of the sheet thickness within 15% of the sheet thickness is ds and d, respectively.
When b is set, it is important that ds / db is 0.95 or less. The lower limit value of ds / db is not particularly limited, but the minimum value of ds / db actually obtained by the present invention is around 0.4.
【００２３】ｄｓ／ｄｂの重要性については、本発明の
実験により明らかとなった。すなわち、請求項１に記載
した鋼組成を満足する鋼を用いて、請求項４に記載の方
法および常法にて、熱間圧延後冷間圧延し、連続焼鈍イ
メージの熱処理を施した冷延鋼板を作製し、ｄｓ／ｄｂ
を種々変化させた冷延鋼板が得た。この冷延鋼板を用い
て冷延鋼板の打ち抜き性とｄｓ／ｄｂの関係について、
調査を行った。なお、打ち抜き性の評価方法としては、
１０ｍｍφのポンチと１０．３ｍｍφのダイス径の打ち
抜き治具にて、板厚０．８ｍｍの冷延鋼板に打ち抜き加
工を施し、打ち抜き穴周辺のバリ高さをポイントマイク
ロメーターにて測定し、バリ高さの大小により、打ち抜
き性を評価した。図１は、ｄｓ／ｄｂとバリ高さとの関
係を示す図である。図１に示すように、ｄｓ／ｄｂを
０．９５以下に制御すれば打ち抜き性の向上が達成でき
ることがわかる。The importance of ds / db has been clarified by experiments of the present invention. That is, using the steel which satisfies the steel composition described in claim 1, cold rolling after cold rolling after hot rolling by the method according to claim 4 and a conventional method, and performing a heat treatment of a continuous annealing image. Prepare steel sheet, ds / db
Was obtained in various ways. Using this cold-rolled steel sheet, the relationship between the punching property of the cold-rolled steel sheet and ds / db is as follows.
A survey was conducted. In addition, as an evaluation method of the punching property,
A 0.8 mm-thick cold-rolled steel plate is punched with a punch of 10 mmφ and a die of 10.3 mmφ, and the burr height around the punched hole is measured with a point micrometer. The punchability was evaluated according to the magnitude of the size. FIG. 1 is a diagram showing the relationship between ds / db and burr height. As shown in FIG. 1, it can be understood that the punching performance can be improved by controlling ds / db to 0.95 or less.
【００２４】上記の成分組成範囲及び金属組織に調整す
ることにより、打ち抜き性に優れる冷延鋼板を得ること
が可能となる。このような特性の鋼は以下の製造方法に
より製造することができる。By adjusting the composition range and the metal structure as described above, it is possible to obtain a cold rolled steel sheet having excellent punching properties. Steel having such characteristics can be manufactured by the following manufacturing method.
【００２５】（３）鋼板製造工程 上記の成分組成範囲に調整した鋼を転炉にて溶製した
後、連続鋳造によりスラブにし、１０００〜１２００℃
に加熱する。(3) Steel plate manufacturing process After the steel adjusted to the above-mentioned component composition range is melted in a converter, it is made into a slab by continuous casting.
Heat to
【００２６】１２００℃を超える加熱温度では、スラブ
中のＴｉＣ，ＴｉＳ，Ｔｉ4 Ｃ2 Ｓ2 析出物がほぼ全量
固溶し、その後の熱延でいかなる工程を施しても、冷延
鋼板で良好な深絞り性は得られない。また、１０００℃
未満の加熱温度では、ＴｉＣ，ＴｉＳ，Ｔｉ4 Ｃ2 Ｓ2
析出物が加熱段階で再固溶することなく、スラブ凝固時
に析出したままの粗大析出物のままであるため、良好な
深絞り性は得られるものの、ＩＦ鋼の不可避的な欠点と
される打ち抜き性は何ら改善されない。従って、加熱温
度は１０００〜１２００℃であり、一部の析出物では粗
大な析出形態を保ちつつ、冷延鋼板での打ち抜き性を改
善するために、一部の析出物を該加熱により再固溶させ
ることが重要となる。At a heating temperature higher than 1200 ° C., almost all of the TiC, TiS, and Ti 4 C 2 S 2 precipitates in the slab form a solid solution. No good deep drawability can be obtained. 1000 ° C
At heating temperatures less than, TiC, TiS, Ti 4 C 2 S 2
Because the precipitate does not re-dissolve in the heating stage and remains as a coarse precipitate during solidification of the slab, good deep drawability can be obtained, but punching, which is an inevitable drawback of IF steel, is obtained. Sex is not improved at all. Accordingly, the heating temperature is 1000 to 1200 ° C., and in order to improve the punching property of a cold-rolled steel sheet while maintaining a coarse precipitation form in some of the precipitates, some of the precipitates are re-solidified by the heating. It is important to dissolve.
【００２７】凝固後そのまま熱間圧延を施す直送圧延の
場合、鋼中に析出するＴｉＣ，ＴｉＳ，Ｔｉ4 Ｃ2 Ｓ2
などＴｉＮ以外の析出物は全体的に微細になりやすく、
その結果ＩＦ鋼特有の良好な深絞り性が得られなくなる
ため、このスラブ加熱処理は必須条件である。なお、打
ち抜き性を向上させるための連続鋳造後の加熱温度の望
ましい範囲は１０００〜１１５０℃である。In the case of direct rolling, in which hot rolling is performed as it is after solidification, TiC, TiS, Ti 4 C 2 S 2 precipitated in steel
Precipitates other than TiN tend to be finer as a whole,
As a result, good deep drawability unique to IF steel cannot be obtained, so that this slab heat treatment is an essential condition. In addition, the desirable range of the heating temperature after continuous casting for improving the punching property is 1000 to 1150 ° C.
【００２８】次に、加熱された鋼をＡｒ3 点以下の温度
域で最終粗圧延を行う、スラブ加熱の際再固溶したＴｉ
Ｃは、粗圧延最終パスをＡｒ3 点以下の温度域で圧延す
ることにより、Ａｒ3 点以下の温度となった粗圧延スラ
ブ表層部で、圧延歪による歪誘起微細析出する。この微
細析出したＴｉＣにより、スラブ表層部で微細フェライ
ト組織を得ることができる。このため、粗圧延後単にα
域に冷却することは、歪誘起析出が起こらないため、微
細析出に対して無意味である。Next, the heated steel is subjected to final rough rolling in a temperature range of not more than 3 points of Ar.
C is the rough rolling final pass by rolling at Ar 3 point or less of the temperature range, the rough rolling a slab surface layer portion became Ar 3 point or less of the temperature and strain-induced fine precipitation by rolling strain. With the finely precipitated TiC, a fine ferrite structure can be obtained in the surface layer of the slab. Therefore, after the rough rolling, simply α
Cooling to a region is meaningless for fine precipitation, since no strain-induced precipitation occurs.
【００２９】その後、粗圧延された鋼をＡｒ3 点以上
（Ａｒ3 ＋１００）℃未満の温度域まで加熱速度５℃／
ｓ以上で望ましくは温度差３０℃以上再加熱し、Ａｒ3
点以上で仕上げ圧延を行い、巻取る。Thereafter, the roughly-rolled steel is heated to a temperature range of not less than the Ar 3 point and less than (Ar 3 +100) ° C. at a heating rate of 5 ° C. /
s or more, desirably a temperature difference of 30 ° C. or more, and Ar 3
Finish rolling at above the point and winding.
【００３０】加熱温度を（Ａｒ3 ＋１００）℃以上とし
た場合および加熱速度を５℃／ｓ未満とした時は、いず
れの場合も微細析出したＴｉＣが再び固溶してしまう。
このため、熱延板中のＴｉＣの析出形態を表層部のみ微
細析出状態とすることが出来ず、表層部が微細なフェラ
イト組織にならず、本発明の効果は十分得られない。When the heating temperature is set to (Ar 3 +100) ° C. or higher and when the heating rate is set to less than 5 ° C./s, the finely precipitated TiC is dissolved again in any case.
For this reason, the precipitation form of TiC in the hot-rolled sheet cannot be made into a fine precipitation state only in the surface layer portion, the surface layer portion does not have a fine ferrite structure, and the effect of the present invention cannot be sufficiently obtained.
【００３１】なお、加熱での制御性等に問題がない限
り、加熱速度の上限はとくに規定されるものではない。
また、粗圧延後の加熱における温度上昇量は３０℃以上
が望ましい。これは、３０℃未満とした場合には、表層
部のみαからγへ再変態させる作用が十分でなく、結果
的に表層部を微細なフェライト組織とすることが出来な
い場合があり、本発明の効果が小さくなることがあるた
めである。Note that the upper limit of the heating rate is not particularly limited as long as there is no problem in controllability or the like in heating.
In addition, the amount of temperature rise in heating after rough rolling is desirably 30 ° C. or more. This is because if the temperature is lower than 30 ° C., the effect of retransforming only the surface layer from α to γ is not sufficient, and as a result, the surface layer may not have a fine ferrite structure. This is because the effect may be reduced.
【００３２】最後に、Ａｒ3 点以上で仕上げ圧延を終了
することに対しては、Ａｒ3 点未満で仕上げた場合、Ｉ
Ｆ鋼特有の良好な深絞り性が得られないため、Ａｒ3 点
以上で仕上げ圧延を終了する必要がある。Finally, with respect to terminating finish rolling at three or more Ar points, if finishing at less than three Ar points,
Since good deep drawability unique to F-steel cannot be obtained, finish rolling needs to be completed at three or more Ar points.
【００３３】以上に述べた限定した条件により、粗圧延
材の表層のみをγからαへ変態させ、５℃／ｓ以上の加
熱速度によりＡｒ3 点以上に再加熱することにより、表
層部のみαからγへ再変態させる。この粗圧延材表層の
受けるγ→α→γ変態と微細ＴｉＣを表層部に集中して
析出させることにより、冷延鋼板における表層部を微細
なフェライト組織とすることが可能となる。Under the above-described limited conditions, only the surface layer of the rough rolled material is transformed from γ to α, and reheated to Ar 3 or more at a heating rate of 5 ° C./s or more, so that only the surface layer has α From γ to γ. By transforming the γ → α → γ transformation and the fine TiC received by the surface layer of the rough rolled material in a concentrated manner on the surface layer, the surface layer of the cold rolled steel sheet can have a fine ferrite structure.
【００３４】巻取り温度については、特に規定されるも
のではないが、ＩＦ鋼特有の高深絞り性を確保するため
に、６００〜７００℃とすることが望ましい。次に、巻
取った熱延鋼板を冷延し、再結晶温度〜８５０℃で焼鈍
し、１．５％以下の調圧率で調質圧延を行う。焼鈍につ
いては再結晶温度〜８５０℃以下で連続焼鈍する。８５
０℃を超えると、γ相へのＣの再固溶を生じ、伸びの低
下を招く。一方、再結晶温度未満では、結晶粒が細か
く、良好な集合組織が発達せず、ｒ値が低くなり、成形
性が悪くなる。また、調質圧延は、冷延鋼板の表面粗さ
制御を目的とし、１．５％以下の調圧率にて行う。ここ
で、調圧率が１．５％を超えると伸び等の材質が劣化す
るため、調圧率は１．５％以下である。The winding temperature is not particularly limited, but is preferably set to 600 to 700 ° C. in order to secure the high deep drawability unique to IF steel. Next, the rolled hot-rolled steel sheet is cold-rolled, annealed at a recrystallization temperature of 850 ° C., and temper-rolled at a pressure control rate of 1.5% or less. Annealing is performed continuously at a recrystallization temperature of 850 ° C. or lower. 85
When the temperature exceeds 0 ° C., C is re-dissolved in the γ phase to cause a decrease in elongation. On the other hand, when the temperature is lower than the recrystallization temperature, the crystal grains are fine, a good texture is not developed, the r value is low, and the formability is poor. The temper rolling is performed at a pressure control rate of 1.5% or less for the purpose of controlling the surface roughness of the cold-rolled steel sheet. Here, when the pressure regulation ratio exceeds 1.5%, the material such as elongation deteriorates, and therefore the pressure regulation ratio is 1.5% or less.
【００３５】また、０．０００２〜０．００１５％のＢ
および０．００５〜０．０３％のＮｂの複合添加によ
り、鋼中の固溶Ｂ，Ｎｂ、場合によっては微細析出Ｎｂ
（Ｃ，Ｎ）により、冷延後再結晶段階での鋼板表層の細
粒化が一層進むため、Ｂ及びＮｂの複合添加は、打ち抜
き性の更なる向上に効果的である。Further, 0.0002 to 0.0015% of B
And the addition of 0.005 to 0.03% Nb to form a solid solution of B and Nb in steel,
(C, N) further refines the surface layer of the steel sheet in the recrystallization stage after cold rolling, so that the combined addition of B and Nb is effective for further improving the punching property.
【００３６】なお、本発明の鋼板は連続焼鈍後、各種電
気めっき処理やそれに加えて有機被覆処理を行った鋼板
ならびに冷間圧延後の鋼板を連続溶融亜鉛めっき処理な
どして、耐食性を向上させた表面処理鋼板などを含み、
これらの鋼板においても十分本発明の効果が得られる。
以下に本発明の実施例を挙げ、本発明の効果を立証す
る。The steel sheet of the present invention is subjected to continuous galvanizing of a steel sheet which has been subjected to various electroplating treatments and an organic coating treatment and a cold-rolled steel sheet after continuous annealing to improve corrosion resistance. Including surface-treated steel sheets,
The effect of the present invention can be sufficiently obtained with these steel sheets.
Hereinafter, examples of the present invention will be described to demonstrate the effects of the present invention.
【００３７】[0037]
（実施例１）表１に実験室溶解炉で出鋼した本発明鋼
（Ｎｏ．１〜１５）及び比較鋼（Ｎｏ．１６〜２１）の
組成を示す。これらの鋼から、実験室熱間圧延用スラブ
を作製し、通常の方法で熱延、酸洗、冷延、連続焼鈍を
行い、冷延鋼板を得た。これらの冷延鋼板から組織観察
用サンプル及び打ち抜き評価用サンプルを採取し、組織
観察、打ち抜き性及びｍｅａｎ−ｒ値を調査した。打ち
抜き性の評価方法は上記に記載の方法と同一とした。(Example 1) Table 1 shows the compositions of the steels of the present invention (Nos. 1 to 15) and comparative steels (Nos. 16 to 21) produced in a laboratory melting furnace. From these steels, slabs for laboratory hot rolling were prepared, and hot rolled, pickled, cold rolled, and continuously annealed by ordinary methods to obtain cold rolled steel sheets. Samples for structure observation and samples for punching evaluation were collected from these cold-rolled steel sheets, and the structure observation, punchability, and mean-r value were investigated. The method for evaluating the punching property was the same as the method described above.
【００３８】ｍｅａｎ−ｒ値は、ＪＩＳ５号引張試験片
を鋼板の圧延方向、圧延方向に対して４５度方向、９０
度方向に採取し、それぞれのｒ値、ｒ0 、ｒ45、ｒ90を
１５％の予歪みを加えて測定した後に、ｍｅａｎ−ｒ＝
（ｒ0 ＋２ｒ45＋ｒ90）／４により算出した。The mean-r value was determined by measuring the JIS No. 5 tensile test piece in the rolling direction of the steel sheet, in a direction at 45 degrees with respect to the rolling direction, at 90 degrees.
After sampling in the degree direction and measuring the respective r values, r 0 , r 45 , and r 90 with a pre-strain of 15%, the mean-r =
It was calculated by (r 0 + 2r 45 + r 90 ) / 4.
【００３９】表１に鋼成分に加えて、組織観察結果（ｄ
ｓ／ｄｂ）、バリ高さ及びｍｅａｎ−ｒ値を示す。表１
から、本発明の鋼組成を満足し、かつフェライト粒径を
満足させる本発明鋼Ｎｏ．１〜１５においては、バリ高
さが０．０３ｍｍ以下の良好な打ち抜き性が得られると
同時に良好な深絞り特性も付与される。Table 1 shows the results of microstructure observation (d
s / db), burr height and mean-r value. Table 1
From the results, it is clear that the steel No. of the present invention satisfying the steel composition of the present invention and satisfying the ferrite grain size. In Nos. 1 to 15, a good punching property with a burr height of 0.03 mm or less is obtained, and also a good deep drawing property is provided.
【００４０】一方、比較鋼Ｎｏ．１６は本発明の組成を
満足するもののｄｓ／ｄｂ値が０．９５を超えるため、
打ち抜き性は良好でない。また、Ｎｏ．１７〜２１の比
較鋼はＣ，Ｔｉ，Ｎｂ，Ｂの各元素が本発明の範囲を満
たしていない。この場合には、フェライト組織は全板厚
にわたり均一になるため、ｄｓ／ｄｂ値は０．９５を上
回り、打ち抜き性が劣化する。また、深絞り性について
はＴｉ添加量の多い鋼Ｎｏ．１８を除きＩＦ鋼特有の高
いｍｅａｎ−ｒ値が得られないことがわかる。On the other hand, the comparative steel No. 16 satisfies the composition of the present invention but has a ds / db value of more than 0.95.
The punchability is not good. In addition, No. In the comparative steels Nos. 17 to 21, the elements C, Ti, Nb, and B did not satisfy the scope of the present invention. In this case, since the ferrite structure becomes uniform over the entire thickness, the ds / db value exceeds 0.95, and the punching property is deteriorated. Regarding the deep drawability, the steel No. It is understood that a high mean-r value peculiar to the IF steel cannot be obtained except for No. 18.
【００４１】[0041]
【表１】 [Table 1]
【００４２】（実施例２）表１に示した本発明鋼の中の
鋼Ｎｏ．１，４，８，１２の４種を選び、これらの成分
を有する実験室鋳造スラブを用い、種々の条件にて熱間
圧延を実施した。その後、常法に従って、酸洗、冷間圧
延を行った後、８３０℃にて連続焼鈍をシミュレートし
た熱処理を施し、最後に１％の調質圧延を行った。その
後、得られた冷延鋼板から、組織観察用サンプル、打ち
抜き性評価用サンプルを採取して、各種確性試験を実施
した。(Example 2) Steel No. 1 in the steel of the present invention shown in Table 1 was used. Four types 1, 4, 8, and 12 were selected, and hot rolling was carried out under various conditions using a laboratory cast slab having these components. Then, after performing pickling and cold rolling according to a conventional method, a heat treatment simulating continuous annealing was performed at 830 ° C., and finally, 1% temper rolling was performed. Thereafter, a sample for structure observation and a sample for punchability evaluation were collected from the obtained cold-rolled steel sheet and subjected to various accuracy tests.
【００４３】表２に示すとおり、（１）スラブ加熱温度
が１０００〜１１５０℃、（２）粗圧延最終パスがＡｒ
3 点以下、（３）粗圧延材の加熱速度が５℃／ｓ以上、
（４）粗圧延材の加熱到達温度がＡｒ3 点以上（Ａｒ3
＋１００）℃未満、（５）仕上圧延温度がＡｒ3 点以上
の本発明の各製造条件のいずれか１つを満足しない条件
である比較例Ｎｏ．２〜５，７〜１０，１２〜１５，１
７〜２０では、ｄｓ／ｄｂの値は０．９５以下を満足し
ない。このため、バリ高さは０．０４ｍｍを超える高い
値となり、打ち抜き性は良好でない。一方、上記（１）
〜（５）の全ての条件を満足する本発明例Ｎｏ．１，
６，１１，１６では、ｄｓ／ｄｂ値が０．９５以下であ
り、バリ高さが０．０３ｍｍ以下という極めて優れた打
ち抜き性を有する冷延鋼板が得られることは明らかであ
る。As shown in Table 2, (1) the slab heating temperature is 1000 to 1150 ° C., and (2) the final pass of the rough rolling is Ar.
3 points or less, (3) heating rate of rough rolled material is 5 ° C / s or more,
(4) The ultimate temperature of heating of the rough rolled material is Ar 3 or more (Ar 3
Comparative Example No. 5 which is less than (+100) ° C. and (5) the finish rolling temperature does not satisfy any one of the production conditions of the present invention in which Ar is 3 points or more. 2-5,7-10,12-15,1
In the range of 7 to 20, the value of ds / db does not satisfy 0.95 or less. For this reason, the burr height is a high value exceeding 0.04 mm, and the punching property is not good. On the other hand, (1)
Inventive Example No. 5 satisfying all the conditions of (1) to (5). 1,
In Nos. 6, 11, and 16, it is clear that a cold rolled steel sheet having an extremely excellent punching property with a ds / db value of 0.95 or less and a burr height of 0.03 mm or less can be obtained.
【００４４】以上から、上記（１）〜（５）の本発明の
各製造条件を全て満たすことは、ＩＦ鋼冷延鋼板に優れ
た打ち抜き性を付与するための重要な製造因子であるこ
とを示している。From the above, it is understood that satisfying all the production conditions of the present invention (1) to (5) is an important production factor for imparting excellent punchability to an IF steel cold-rolled steel sheet. Is shown.
【００４５】[0045]
【表２】 [Table 2]
【００４６】[0046]
【発明の効果】本発明によれば、鋼組成、金属組織及び
製造条件を特定することにより、材質が劣化することな
く、優れた打ち抜き特性を有する各種ＩＦ鋼冷延鋼板を
提供することができ、工業上優れた効果がもたらされ
る。According to the present invention, it is possible to provide various IF steel cold-rolled steel sheets having excellent punching characteristics without deteriorating the material by specifying the steel composition, metal structure, and manufacturing conditions. In addition, an industrially superior effect is brought.
【図１】本発明の実施の形態に係るｄｓ／ｄｂとバリ高
さとの関係を示す図。FIG. 1 is a diagram showing a relationship between ds / db and burr height according to an embodiment of the present invention.
Claims (6)
ｉ：０．３％以下と、Ｍｎ：０．０５〜０．５％と、
Ｐ：０．０３％以下と、Ｓ：０．００３〜０．０１５％
と、Ｓｏｌ．Ａｌ：０．０３〜０．０６％と、Ｔｉ：
０．０２〜０．０８％と、Ｎ：０．００３％以下とを含
有し、鋼板表面から板厚１５％以内の表層部と鋼板表面
から板厚１５％以内を除いた板厚中心部における平均フ
ェライト粒径をそれぞれｄｓ、ｄｂとするとき、ｄｓ／
ｄｂが０．９５以下であることを特徴とする打ち抜き性
に優れる冷延鋼板。1. The method according to claim 1, wherein C: 0.003% or less in weight%,
i: 0.3% or less, Mn: 0.05 to 0.5%,
P: 0.03% or less, S: 0.003 to 0.015%
And Sol. Al: 0.03-0.06%, Ti:
0.02 to 0.08% and N: 0.003% or less, in the surface layer portion having a thickness of 15% or less from the surface of the steel sheet and in the central portion of the thickness of the sheet excluding the thickness of 15% or less from the steel surface When the average ferrite grain size is ds and db, respectively, ds /
A cold rolled steel sheet having excellent punchability, wherein db is 0.95 or less.
０．００１５％を含有することを特徴とする請求項１に
記載の打ち抜き性に優れる冷延鋼板。2. B: 0.0002-% by weight
The cold-rolled steel sheet having excellent punchability according to claim 1, wherein the steel sheet contains 0.0015%.
０．０３％を含有することを特徴とする請求項１または
２に記載の打ち抜き性に優れる冷延鋼板。3. Nb: 0.005 to 5% by weight.
The cold rolled steel sheet having excellent punchability according to claim 1 or 2, which contains 0.03%.
法において、 連続鋳造した鋼を１０００〜１２００℃に加熱する工程
と、 加熱された鋼をＡｒ3 点以下の温度域で最終粗圧延を行
う工程と、 粗圧延された鋼をＡｒ3 点以上（Ａｒ3 ＋１００）℃未
満の温度域まで加熱速度５℃／ｓ以上で再加熱し、Ａｒ
3 点以上で仕上げ圧延を行い、巻取る工程と、 巻取った熱延鋼板を冷延し、再結晶温度〜８５０℃で焼
鈍し、１．５％以下の調圧率で調質圧延を行う工程と、 を備えたことを特徴とする打ち抜き性に優れる冷延鋼板
の製造方法。4. The method for producing a cold-rolled steel sheet according to claim 1, wherein the continuously cast steel is heated to 1000 to 1200 ° C., and the heated steel is subjected to a final roughing process in a temperature range of 3 points or less of Ar. Rolling and re-heating the roughly-rolled steel at a heating rate of 5 ° C./s or more to a temperature range of not less than Ar 3 points and less than (Ar 3 +100) ° C.
Finish rolling at three or more points, winding step, cold rolling of hot rolled steel sheet, annealing at recrystallization temperature ~ 850 ° C, and temper rolling at 1.5% or less pressure control rate A method for producing a cold-rolled steel sheet having excellent punching characteristics, comprising:
００２〜０．００１５％を含有していることを特徴とす
る請求項４に記載の打ち抜き性に優れる冷延鋼板の製造
方法。5. The steel sheet further comprises B: 0.0% by weight.
The method for producing a cold-rolled steel sheet having excellent punchability according to claim 4, which contains 002 to 0.0015%.
００５〜０．０３％を含有していることを特徴とする請
求項４または５に記載の打ち抜き性に優れる冷延鋼板の
製造方法。6. The steel sheet may further contain Nb: 0.
The method for producing a cold-rolled steel sheet having excellent punchability according to claim 4, wherein the method comprises 005 to 0.03%.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32964996A JP3355970B2 (en) | 1996-12-10 | 1996-12-10 | Manufacturing method of cold rolled steel sheet with excellent punchability |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32964996A JP3355970B2 (en) | 1996-12-10 | 1996-12-10 | Manufacturing method of cold rolled steel sheet with excellent punchability |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2002155489A Division JP2003041342A (en) | 2002-05-29 | 2002-05-29 | Cold rolled steel sheet superior in stamping property |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH10168544A true JPH10168544A (en) | 1998-06-23 |
| JP3355970B2 JP3355970B2 (en) | 2002-12-09 |
Family
ID=18223712
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32964996A Expired - Fee Related JP3355970B2 (en) | 1996-12-10 | 1996-12-10 | Manufacturing method of cold rolled steel sheet with excellent punchability |
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| Country | Link |
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| JP (1) | JP3355970B2 (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001073079A (en) * | 1999-07-05 | 2001-03-21 | Kawasaki Steel Corp | Extra-low carbon thin steel sheet for deep drawing and extra-low carbon thin steel sheet for deep drawing applied with galvanizing |
| CN104264046A (en) * | 2014-09-10 | 2015-01-07 | 河北钢铁股份有限公司唐山分公司 | Production method of ultralow-carbon interstitial free soft steel |
| CN105603299A (en) * | 2016-02-03 | 2016-05-25 | 首钢总公司 | Extra-deep drawing interstitial free steel and production method thereof |
| WO2021065346A1 (en) | 2019-10-01 | 2021-04-08 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| WO2021182395A1 (en) | 2020-03-11 | 2021-09-16 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| WO2022044494A1 (en) | 2020-08-27 | 2022-03-03 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| WO2022044493A1 (en) | 2020-08-27 | 2022-03-03 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| KR20220111724A (en) | 2020-01-27 | 2022-08-09 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| KR20230035624A (en) | 2020-08-27 | 2023-03-14 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| WO2023038084A1 (en) | 2021-09-08 | 2023-03-16 | 日本製鉄株式会社 | Hot-rolled steel sheet |
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| JPH0931597A (en) * | 1995-07-14 | 1997-02-04 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet excellent in deep drawability and blankability |
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Cited By (15)
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|---|---|---|---|---|
| JP2001073079A (en) * | 1999-07-05 | 2001-03-21 | Kawasaki Steel Corp | Extra-low carbon thin steel sheet for deep drawing and extra-low carbon thin steel sheet for deep drawing applied with galvanizing |
| CN104264046A (en) * | 2014-09-10 | 2015-01-07 | 河北钢铁股份有限公司唐山分公司 | Production method of ultralow-carbon interstitial free soft steel |
| CN105603299A (en) * | 2016-02-03 | 2016-05-25 | 首钢总公司 | Extra-deep drawing interstitial free steel and production method thereof |
| KR20220050206A (en) | 2019-10-01 | 2022-04-22 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| WO2021065346A1 (en) | 2019-10-01 | 2021-04-08 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| KR20220111724A (en) | 2020-01-27 | 2022-08-09 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| KR20220134776A (en) | 2020-03-11 | 2022-10-05 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| WO2021182395A1 (en) | 2020-03-11 | 2021-09-16 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| WO2022044493A1 (en) | 2020-08-27 | 2022-03-03 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| WO2022044494A1 (en) | 2020-08-27 | 2022-03-03 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| KR20230035624A (en) | 2020-08-27 | 2023-03-14 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| KR20230040349A (en) | 2020-08-27 | 2023-03-22 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| KR20230041055A (en) | 2020-08-27 | 2023-03-23 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel |
| WO2023038084A1 (en) | 2021-09-08 | 2023-03-16 | 日本製鉄株式会社 | Hot-rolled steel sheet |
| KR20240038998A (en) | 2021-09-08 | 2024-03-26 | 닛폰세이테츠 가부시키가이샤 | hot rolled steel plate |
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