JPH04371528A - Production of cold rolled steel sheet for deep drawing - Google Patents
Production of cold rolled steel sheet for deep drawingInfo
- Publication number
- JPH04371528A JPH04371528A JP3171836A JP17183691A JPH04371528A JP H04371528 A JPH04371528 A JP H04371528A JP 3171836 A JP3171836 A JP 3171836A JP 17183691 A JP17183691 A JP 17183691A JP H04371528 A JPH04371528 A JP H04371528A
- Authority
- JP
- Japan
- Prior art keywords
- rolled steel
- cold
- rolled
- deep drawing
- steel sheet
- 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.)
- Granted
Links
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 33
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 41
- 239000010959 steel Substances 0.000 claims abstract description 41
- 238000000034 method Methods 0.000 claims abstract description 28
- 238000005098 hot rolling Methods 0.000 claims abstract description 26
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 22
- 229910052802 copper Inorganic materials 0.000 claims abstract description 19
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 17
- 238000010438 heat treatment Methods 0.000 claims abstract description 15
- 229910052742 iron Inorganic materials 0.000 claims abstract description 11
- 238000000137 annealing Methods 0.000 claims abstract description 10
- 238000009628 steelmaking Methods 0.000 claims abstract description 4
- 229910052717 sulfur Inorganic materials 0.000 claims description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 238000005261 decarburization Methods 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 abstract description 17
- 229910052759 nickel Inorganic materials 0.000 abstract description 15
- 229910001209 Low-carbon steel Inorganic materials 0.000 abstract description 6
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 238000005097 cold rolling Methods 0.000 abstract description 5
- 230000001771 impaired effect Effects 0.000 abstract description 3
- 238000004804 winding Methods 0.000 description 13
- 230000001105 regulatory effect Effects 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 238000001953 recrystallisation Methods 0.000 description 5
- 230000006866 deterioration Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000004615 ingredient Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- -1 first Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は深絞り用冷延鋼板の製造
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 cold-rolled steel sheets for deep drawing.
【０００２】0002
【従来の技術】Ｔｉを添加した極低炭素鋼を用いた深絞
り用冷延鋼板の製造方法としては、数多くありその代表
的なものとしては特公昭４４−１８０６６号公報がある
。最近、廃棄された自動車など鉄スクラップが増え、製
鉄業の鉄源として見直されつつある。しかし、鉄スクラ
ップに含有されるＣｕ，Ｓｎ，Ｎｉ，Ｃｒ，等は通常の
精錬法では除去することが困難であり、鋼の中にそれら
のトランプエレメントは残留し品質が劣化する。そのた
め、Ｔｉを添加した極低炭素鋼を用いるような高級グレ
ードの深絞り用冷延鋼板の製造方法には特公昭４４−１
８０６６号公報を初めとする従来の技術ではこれらのト
ランプエレメントは許容されておらず、鉄スクラップは
使用されなかった。2. Description of the Related Art There are many methods for producing cold-rolled steel sheets for deep drawing using ultra-low carbon steel added with Ti, and a representative example is Japanese Patent Publication No. 18066/1983. Recently, the amount of iron scrap such as discarded automobiles has increased, and it is being reconsidered as a source of iron for the steel industry. However, Cu, Sn, Ni, Cr, etc. contained in iron scrap are difficult to remove by normal refining methods, and these tramp elements remain in the steel, resulting in deterioration of quality. Therefore, the manufacturing method of high-grade cold-rolled steel sheets for deep drawing using ultra-low carbon steel with addition of Ti is
Conventional techniques such as Japanese Patent No. 8066 do not allow these playing card elements and do not use scrap iron.
【０００３】0003
【発明が解決しようとする課題】本発明で解決しようと
する課題は、Ｃｕ，Ｓｎ，Ｎｉ，Ｃｒ，がトランプエレ
メントとして残留する鋳片を用いても、深絞り性が損な
われない深絞り用冷延鋼板の製造方法を提供する事であ
る。[Problems to be Solved by the Invention] The problem to be solved by the present invention is to provide a deep-drawing product that does not impair deep drawability even when using a slab in which Cu, Sn, Ni, and Cr remain as tramp elements. The object of the present invention is to provide a method for manufacturing cold-rolled steel sheets.
【０００４】0004
【課題を解決するための手段】本発明者等は、Ｃｕ，Ｓ
ｎ，Ｎｉ，Ｃｒ，がトランプエレメントとして残留する
鋳片を用いても、深絞り性が損なわれない深絞り用冷延
鋼板の製造方法に付いて、種々検討し、本発明の方法を
見いだしたものである。本発明の要旨は下記の通りであ
る。
（１）製鋼（溶製、脱炭、鋳造）工程で鉄源の一部又は
全量をスクラップで賄う方法でスラブを造り、連続熱延
、冷間圧延、再結晶焼鈍、調質圧延（以下Ｓ．Ｐと記す
）の工程を経て冷延鋼板を製造する方法において、Ｃ≦
０．００８％，Ｓｉ≦０．６０％，Ｍｎ≦０．８０％，
Ｐ≦０．１２０％，Ｓ≦０．０３５％，ｓｏｌＡｌ≦０
．１００％，Ｎ≦０．００８０％，Ｔｉ：０．０１０〜
０．１０％，Ｂ≦０．００２０％，及びトランプエレメ
ントとしてＣｕ：０．０５〜０．２０，Ｓｎ：０．００
５〜０．０２０，且つＣｕ（％）×Ｓｎ（％）≦０．０
０２，Ｎｉ≦０．３％，Ｃｒ≦０．２％、残部不可避的
不純物及び鉄よりなる鋼片を、通常の方法で加熱し連続
熱延を行い６７０〜８００℃で巻き取り熱延鋼帯とし、
冷間圧延を行い、その後、連続焼鈍にて再結晶焼鈍を行
なった後、Ｓ．Ｐを施すことを特徴とする深絞り用冷延
鋼板の製造方法。
（２）熱間圧延時のスラブ加熱温度を１１５０℃以下で
行い、熱延後の巻き取り温度を８００℃以下とする請求
項１記載の方法。[Means for solving the problem] The present inventors have discovered that Cu, S
The present inventors conducted various studies on a method for producing cold-rolled steel sheets for deep drawing in which the deep drawability is not impaired even when using slabs in which n, Ni, and Cr remain as trump elements, and the method of the present invention was discovered. It is something. The gist of the invention is as follows. (1) Slabs are made by using scrap as part or all of the iron source in the steelmaking (melting, decarburization, and casting) process, and are continuously hot rolled, cold rolled, recrystallized annealed, and temper rolled (hereinafter referred to as S). In the method of manufacturing a cold rolled steel sheet through the process of (denoted as P), C≦
0.008%, Si≦0.60%, Mn≦0.80%,
P≦0.120%, S≦0.035%, solAl≦0
．． 100%, N≦0.0080%, Ti: 0.010~
0.10%, B≦0.0020%, and as a playing card element Cu: 0.05-0.20, Sn: 0.00
5 to 0.020, and Cu (%) x Sn (%)≦0.0
02. A steel billet consisting of Ni≦0.3%, Cr≦0.2%, the remainder containing unavoidable impurities and iron is heated in a conventional manner and continuously hot rolled, then wound at 670 to 800°C to produce a hot rolled steel strip. year,
After performing cold rolling and then recrystallization annealing by continuous annealing, S. A method for producing a cold-rolled steel sheet for deep drawing, characterized by applying P. (2) The method according to claim 1, wherein the heating temperature of the slab during hot rolling is 1150°C or lower, and the coiling temperature after hot rolling is 800°C or lower.
【０００５】以下に本発明について詳細に述べる。本発
明者等は、Ｔｉ添加極低炭素鋼にＣｕ，Ｓｎ，Ｎｉ，Ｃ
ｒを単独或いは複合添加した鋼を造り、熱延条件を変え
深絞り性に及ぼす影響に付いて種々検討した結果、図１
，図２に示すように、以下のことが明らかになった。
■トランプエレメントを含有する鋼は１２００℃に加熱
し熱延後５００〜６５０℃巻き取る通常の熱延方法では
深絞り性が著しく劣化し、深絞り用冷延鋼板が製造出来
ないこと。■トランプエレメントの含有量を請求項（１
）に規制した上で、（１）熱間圧延条件を通常の方法で
加熱し連続熱延を行い６７０〜８００℃で巻き取り熱延
鋼帯とする方法、（２）熱間圧延時のスラブ加熱温度を
１１５０℃以下で行い、熱延後の８００℃以下で巻き取
り熱延鋼帯とする方法、の何れかの方法を採用すること
によって、Ｃｕ，Ｓｎ，Ｎｉ，Ｃｒ，がトランプエレメ
ントとして残留する鋳片を用いても、深絞り性が劣化せ
ず深絞り用冷延鋼板が製造出来ること。この様に、６７
０℃以上で巻き取る方法或いは１１５０℃以下の加熱温
度とする方法によって上述のように深絞り性を示すｒ値
がトランプエレメントが増加しても低下しなくなるメカ
ニズムはまだ充分には解明されておらず今後の検討が必
要である。尚、図１，図２は、０．０４％のＴｉを添加
したＣ：０．００２％の極低炭素鋼にＣｕ：０．１２％
，Ｓｎ：０．０１０％，Ｎｉ：０．１０％，Ｃｒ：０．
０５％を添加し、熱延条件を変えて熱延鋼板を製造し、
８０％の冷延率で冷延し７７５℃×６０ｓの再結晶焼鈍
を行った後０．８％のＳ．Ｐを施して０．８ｍｍの冷延
鋼板を造りｒ値を測定した結果を図に示したものである
。一方、Ｃｕ，Ｓｎ含有鋼の熱間脆性起因の冷延鋼板の
表面傷（線状でスケールの咬み込みを伴う凹み傷）に付
いても調査検討した結果、Ｃｕ≦０．２０，Ｓｎ≦０．
０２０，且つＣｕ（％）×Ｓｎ（％）≦０．００２，に
規制すれば、表面傷の発生も防止でき表面品位の良好な
深絞り用冷延鋼板が得られることがわかった。The present invention will be described in detail below. The present inventors added Cu, Sn, Ni, and C to Ti-added ultra-low carbon steel.
As a result of various studies on the effects on deep drawability of steels made with r added either singly or in combination and by changing the hot rolling conditions, the results shown in Figure 1
, As shown in Figure 2, the following was clarified. (2) With the usual hot rolling method in which steel containing tramp elements is heated to 1200°C, hot-rolled and then rolled at 500 to 650°C, the deep drawability deteriorates significantly, making it impossible to produce cold-rolled steel sheets for deep drawing. ■Claim the content of playing card elements (1)
), (1) the hot rolling condition is a method of continuous hot rolling by heating in a normal manner and winding at 670 to 800°C to form a hot rolled steel strip, (2) a method of hot rolling to form a hot rolled steel strip; Cu, Sn, Ni, Cr, etc. can be used as playing elements by adopting one of the following methods: heating at a temperature of 1150°C or lower and winding the hot-rolled steel strip at a temperature of 800°C or lower after hot rolling. To be able to produce cold rolled steel sheets for deep drawing without deteriorating deep drawability even if remaining slabs are used. Like this, 67
The mechanism by which the r-value, which indicates deep drawability, does not decrease even when the number of tramp elements increases, as described above, by a method of winding at 0°C or higher or a heating temperature of 1150°C or lower has not yet been fully elucidated. Further consideration is required. In addition, Figures 1 and 2 show ultra-low carbon steel with 0.002% C and 0.04% Ti added with 0.12% Cu.
, Sn: 0.010%, Ni: 0.10%, Cr: 0.
05% was added and hot-rolled steel sheets were manufactured by changing the hot-rolling conditions.
After cold rolling at a cold rolling rate of 80% and recrystallization annealing at 775°C for 60 seconds, an S.I. of 0.8% was applied. The figure shows the results of measuring the r value of a 0.8 mm cold rolled steel plate subjected to P treatment. On the other hand, as a result of investigating and examining the surface flaws (linear indentation flaws with scale bite) on cold-rolled steel sheets caused by the hot embrittlement of Cu and Sn-containing steels, we found that Cu≦0.20, Sn≦0 ．．
020 and Cu (%) x Sn (%)≦0.002, it was found that the occurrence of surface scratches could be prevented and a cold-rolled steel sheet for deep drawing with good surface quality could be obtained.
【０００６】以下に製造条件について詳細に述べる。鋼
の成分としては、先ず、トランプエレメント以外のＴｉ
添加極低炭素鋼の成分は従来から行われている成分でよ
く特に規制する必要はなく、Ｃ≦０．００８％，Ｓｉ≦
０．６０％，Ｍｎ≦０．８０％，Ｐ≦０．１２０％，Ｓ
≦０．０３５％，ｓｏｌＡｌ≦０．１００％，Ｎ≦０．
００８０％，Ｔｉ：０．０１０〜０．１０％，Ｂ≦０．
００２０％，の含有量であればよく、Ｃ，Ｓｉ，Ｍｎ，
Ｐ，Ｓ，ｓｏｌＡｌ，Ｎ，Ｔｉ，Ｂは、何れもこれらの
値以上に含有すると焼鈍時の結晶粒の成長性が悪化して
ｒ値が低下し深絞り用冷延鋼板が得られなくなる。尚、
Ｔｉは再結晶時に結晶粒の方位を制御し深絞り性を向上
させるのに極めて有効な元素で０．０１０％以上必要で
あるので下限値を０．０１０％とした。又、Ｂは深絞り
プレス加工後更に二次加工を加えた時の脆性割れ感受性
（以下二次加工性と記す）を改善したいときに０．００
２０％以下の範囲で添加すればよい。Ｃ，Ｓｉ，Ｍｎ，
Ｐ，Ｓ，ｓｏｌＡｌおよびＮは少なければ少ないほど深
絞り性が向上するので下限を規制する必要がない。Ｃｕ
，Ｓｎ，Ｎｉ，Ｃｒは、通常の熱延条件では含有量が増
えるに従って著しい深絞り性の低下が起こり深絞り用冷
延鋼板の製造が出来なくなるが、本発明の請求項（１）
及び（２）の熱延条件では、トランプエレメントとして
Ｃｕ：０．０５〜０．２０，Ｓｎ：０．００５〜０．０
２０，且つＣｕ（％）×Ｓｎ（％）≦０．００２，Ｎｉ
≦０．３％，Ｃｒ≦０．２％に規制した成分とする事に
よって深絞り性の劣化を回避出来、深絞り用冷延鋼板の
製造が可能となる。尚、Ｃｕ，Ｓｎ，のトランプエレメ
ントとしての含有量に下限をもうけたのは、Ｃｕが０．
０５％未満で且つＳｎが０．００５％未満の範囲では、
本願の発明の熱延条件を採用せずに通常の熱延条件で製
造しても深絞り性の劣化は許容限界内であり深絞り用冷
延鋼板の製造が可能であるので、Ｃｕ，Ｓｎの下限値を
Ｃｕ≧０．０５％，Ｓｎ≧０．００５％とした。尚、Ｎ
ｉ，Ｃｒの含有量に下限をもうけなかったのは、Ｎｉ，
Ｃｒは鉄スクラップを選定すればトランプエレメントと
しての混入をかなり抑制できるので特に下限値を設けな
かった。又、Ｃｕ，Ｓｎは、深絞り性を顕著に劣化させ
るばかりではなく、多く含まれると、Ｃｕ，Ｓｎ含有鋼
の熱間脆性起因の表面傷が発生し、自動車などに使用さ
れる深絞り用冷延鋼板が得られなくなるので、この点に
於いても、Ｃｕ≦０．２０，Ｓｎ≦０．０２０，且つＣ
ｕ（％）×Ｓｎ（％）≦０．００２，に規制することが
重要である。連続鋳造条件は、Ｃｕ及びＳｎ含有量を本
発明の範囲に規制すれば、特に規制する必要がなく通常
の条件で鋳片を製造すればよい。[0006] Manufacturing conditions will be described in detail below. As for the components of steel, first, Ti other than the tramp element is
The ingredients of additive ultra-low carbon steel are conventional ingredients and there is no need to particularly regulate them, C≦0.008%, Si≦
0.60%, Mn≦0.80%, P≦0.120%, S
≦0.035%, solAl≦0.100%, N≦0.
0080%, Ti: 0.010-0.10%, B≦0.
0020%, C, Si, Mn,
If any of P, S, solAl, N, Ti, and B is contained in amounts exceeding these values, the growth of crystal grains during annealing will deteriorate, the r value will decrease, and a cold rolled steel sheet for deep drawing will not be obtained. still,
Ti is an extremely effective element for controlling the orientation of crystal grains during recrystallization and improving deep drawability, and since 0.010% or more is required, the lower limit was set at 0.010%. In addition, B is 0.00 when you want to improve the brittle crack susceptibility (hereinafter referred to as secondary workability) when secondary processing is added after deep drawing press processing.
It may be added within a range of 20% or less. C, Si, Mn,
The smaller the amount of P, S, solAl, and N, the better the deep drawability is, so there is no need to regulate the lower limit. Cu
, Sn, Ni, and Cr, as their content increases under normal hot rolling conditions, the deep drawability deteriorates significantly and it becomes impossible to produce cold rolled steel sheets for deep drawing.
In hot rolling conditions (2), Cu: 0.05 to 0.20, Sn: 0.005 to 0.0 as a playing card element.
20, and Cu (%) × Sn (%)≦0.002, Ni
By regulating the components to ≦0.3% and Cr≦0.2%, deterioration of deep drawability can be avoided, and cold rolled steel sheets for deep drawing can be manufactured. Note that the lower limit was set for the content of Cu and Sn as playing card elements when Cu is 0.
In the range where Sn is less than 0.05% and Sn is less than 0.005%,
Even if manufactured under normal hot rolling conditions without adopting the hot rolling conditions of the invention of the present application, the deterioration of deep drawability is within the permissible limit and it is possible to manufacture cold rolled steel sheets for deep drawing. The lower limits of Cu≧0.05% and Sn≧0.005% were set. Furthermore, N
The reason why no lower limit was set for the content of i, Cr was Ni,
For Cr, if iron scrap is selected, the contamination as a playing card element can be considerably suppressed, so no particular lower limit value was set. In addition, Cu and Sn not only significantly deteriorate the deep drawability, but if they are present in large quantities, surface scratches due to hot embrittlement of Cu and Sn containing steels will occur, making it difficult for deep drawing materials used in automobiles etc. Since a cold rolled steel sheet cannot be obtained, in this respect as well, Cu≦0.20, Sn≦0.020, and C
It is important to regulate u (%)×Sn (%)≦0.002. Continuous casting conditions do not need to be particularly regulated as long as the Cu and Sn contents are regulated within the range of the present invention, and slabs may be manufactured under normal conditions.
【０００７】熱間圧延の条件は、トランプエレメントの
規制と共に本発明の重要なポイントで、（１）熱間圧延
後の巻き取り温度を６７０〜８００℃とする請求項（１
）の方法と、（２）スラブの加熱温度を１１５０℃以下
とする請求項（２）の方法の二通りの方法がある。
請求項（１）のようにスラブの加熱温度を特に規制せず
１１５０℃超で行う場合は、巻き取り温度が６７０℃未
満では、例えトランプエレメントの含有量を請求項（１
）に規制しても深絞り性を示すｒ値が顕著に劣化し深絞
り用冷延鋼板が製造できなくなるので６７０℃以上で巻
き取る必要がある。尚、巻き取り温度が８００℃超にな
るとスケールの膜厚が厚くなりすぎ酸洗性が著しく劣化
するようになるので８００℃以下にする必要がある。請
求項（２）のように巻き取り温度を特に規制せず６７０
℃未満で行う場合は、スラブ加熱温度が１１５０超では
、例えトランプエレメントの含有量を請求項（１）に規
制した範囲に規制しても、深絞り性が顕著に劣化し深絞
り用冷延鋼板が製造できなくなるので、加熱温度を１１
５０℃以下に規制する必要がある。加熱温度を１１５０
℃以下とする事によって巻き取り温度が６７０℃未満と
低くても、Ｃｕ，Ｓｎ，Ｎｉ，Ｃｒ，がトランプエレメ
ントとして残留する鋳片を用いても深絞り性が劣化せず
、深絞り用冷延鋼板が製造出来る。尚、巻き取り温度が
８００℃超になるとスケールの膜厚が厚くなりすぎ酸洗
性が著しく劣化するようになるので巻き取り温度の上限
を８００℃とした。冷延条件は特に規制する必要はなく
通常の深絞り用冷延鋼板に適用される条件でよい。連続
焼鈍条件も特に規制する必要はなく通常の深絞り用冷延
鋼板に適用される条件でよく再結晶焼鈍を行えばよい。
Ｓ．Ｐ条件も特に規制する必要はなく通常の深絞り用冷
延鋼板に適用される条件でよい。尚、本発明は、冷延鋼
板のみならず、電気亜鉛メッキ鋼板の原板、有機皮膜を
被覆した鋼板等の各種の表面処理鋼板の原板の製造方法
としても適用できる。[0007] The hot rolling conditions are important points of the present invention as well as the regulation of the tramp element.
There are two methods. If the heating temperature of the slab is not particularly regulated and is carried out at over 1150°C as in claim (1), if the winding temperature is less than 670°C, even if the content of the playing card element is
), the r-value, which indicates deep drawability, will deteriorate significantly and cold-rolled steel sheets for deep drawing cannot be manufactured, so it is necessary to wind the steel sheet at a temperature of 670°C or higher. It should be noted that if the winding temperature exceeds 800°C, the scale film thickness will become too thick and the pickling properties will be significantly deteriorated, so it is necessary to keep the winding temperature below 800°C. 670 without particularly regulating the winding temperature as in claim (2).
If the slab heating temperature exceeds 1150°C, the deep drawability will deteriorate significantly even if the content of the tramp element is regulated within the range specified in claim (1). Since the steel plate cannot be manufactured, the heating temperature should be set to 11.
It is necessary to regulate the temperature to below 50℃. Heating temperature 1150
℃ or lower, even if the coiling temperature is as low as less than 670℃, the deep drawability will not deteriorate even when using slabs in which Cu, Sn, Ni, Cr, etc. remain as tramp elements. Rolled steel plates can be manufactured. Incidentally, if the winding temperature exceeds 800°C, the scale film thickness becomes too thick and the pickling property deteriorates significantly, so the upper limit of the winding temperature was set at 800°C. The cold rolling conditions do not need to be particularly regulated and may be conditions applied to ordinary cold rolled steel sheets for deep drawing. Continuous annealing conditions do not need to be particularly restricted, and recrystallization annealing may be performed under conditions applicable to ordinary cold-rolled steel sheets for deep drawing. S. There is no need to particularly regulate the P conditions, and conditions applicable to ordinary cold-rolled steel sheets for deep drawing may be used. The present invention can be applied not only to cold-rolled steel sheets but also as a method for manufacturing various surface-treated steel sheets such as electrogalvanized steel sheets and organic film-coated steel sheets.
【０００８】[0008]
【実施例】以下に本発明の効果を実施例により説明する
。表１，２に示す成分の鋳片を、製鋼（溶製、脱炭、鋳
造）工程で鉄源の一部又は全量をスクラップで賄う方法
及び通常の方法で造り、表２に示す熱延条件で熱延し４
．０ｍｍの熱延鋼板を造り、０．８ｍｍに冷間圧延し、
連続焼鈍で均熱温度（以下Ｓ．Ｔと記す）Ｓ．Ｔ×６０
ｓｅｃの再結晶焼鈍を行い、０．６％のＳ．Ｐを施して
冷延鋼板を製造し、深絞り性を示すｒ値の測定と、表面
傷の調査を行った。その結果を表２に示す。EXAMPLES The effects of the present invention will be explained below using examples. Slabs with the components shown in Tables 1 and 2 are made by a method in which part or all of the iron source is provided by scrap in the steelmaking (melting, decarburization, casting) process or by a normal method, and hot rolled under the hot rolling conditions shown in Table 2. Hot rolled with 4
．． A 0mm hot-rolled steel plate was made and cold-rolled to 0.8mm.
Continuous annealing at a soaking temperature (hereinafter referred to as S.T.) S. T×60
sec recrystallization annealing and 0.6% S.I. Cold-rolled steel sheets were produced by applying P, and the r value, which indicates deep drawability, was measured and surface flaws were investigated. The results are shown in Table 2.
【０００９】[0009]
【表１】[Table 1]
【００１０】0010
【表２】[Table 2]
【００１１】鋼Ａはトランプエレメントを含有しない従
来例で通常の深絞り用冷延鋼板の製造条件で製造した例
である。鋼Ｂ，Ｆ，Ｈ，Ｊは、比較例である。鋼Ｃ，Ｄ
，Ｅ，Ｇ，Ｉは何れも本願の発明の方法の成分及びトラ
ンプエレメントの許容範囲内で熱延条件も本願発明の方
法の製造条件のもので、比較例に比べ何れも優れた深絞
り性を示すｒ値が得られており、従来例の鋼Ａと比べて
も遜色のないｒ値が得られ、深絞り用冷延鋼板が製造で
きている。鋼ＢはＣｕ，Ｓｎ，Ｎｉ，Ｃｒをトランプエ
レメントとして含有し、通常の熱延条件で製造された比
較例であり、本願の発明の条件を外れており、ｒ値は１
．５２と低く深絞り用鋼板が得られていない。鋼Ｃ，Ｄ
，Ｅは、鋼Ｂとほぼ同じ成分及びトランブエレメント含
有量の鋼を本発明の熱延条件で製造した例で、鋼Ｃは、
巻き取り温度を７５０℃とした請求項（１）の実施例で
、鋼Ｄは、加熱温度を１５０℃とした請求項（２）の実
施例で、鋼Ｅは、巻き取り温度を７６０℃とし且つ加熱
温度を１０５０℃とした請求項（１）及び（２）の両方
を採用した実施例であり、何れも優れた深絞り性が得ら
れている。鋼ＦはＣｕ，Ｓｎ，Ｎｉ，Ｃｒをトランプエ
レメントとして含有し二次加工性を向上させるためにＢ
を添加し、通常の熱延条件で製造された比較例であり、
本願の発明の条件を外れており、ｒ値は１．４８と低く
二次加工性が要求される用途用の深絞り用鋼板が得られ
ていない。鋼Ｇは、鋼Ｆとほぼ同じ成分及びトランプエ
レメント含有量のＢを添加した二次加工性が要求される
用途用の深絞り用鋼板鋼を製造する本発明の実施例で、
巻き取り温度を７６０℃とし且つ加熱温度を１０５０℃
とした請求項（１）及び（２）の両方を採用した実施例
であり、優れた深絞り性が得られている。鋼Ｈ，ＩはＰ
を添加し深絞り性に優れた高強度鋼板を製造する場合の
通常の熱延条件で製造された比較例の鋼Ｈと、巻き取り
温度を７５０℃とし且つ加熱温度を１０５０℃とした請
求項（１）及び（２）の両方を採用した実施例の鋼Ｉで
ある。鋼Ｈは、本願の発明の条件を外れており、ｒ値は
１．４２と低く深絞り性に優れた高強度鋼板が得られて
いない。鋼Ｉは、ｒ値が１．７５と優れた深絞り性を有
する高強度鋼板が得られている。鋼Ｊは、熱延条件は本
願発明の方法の熱延条件で製造されているが、Ｃｕ，Ｓ
ｎ，Ｎｉ，Ｃｒをトランプエレメントが本願発明の範囲
を越えて含有した比較例で、本願の発明の条件を外れて
おり、ｒ値は１．５５と低く深絞り用鋼板が得られてい
ない。又、表面傷も発生している。Steel A is a conventional example that does not contain a tramp element and is an example manufactured under normal manufacturing conditions for cold-rolled steel sheets for deep drawing. Steels B, F, H, and J are comparative examples. Steel C, D
, E, G, and I are all within the allowable range of the ingredients and tramp element of the method of the invention of the present application, and the hot rolling conditions are also the manufacturing conditions of the method of the invention of the present application, and all have excellent deep drawability compared to the comparative example. An r value that is comparable to that of conventional steel A was obtained, and a cold-rolled steel sheet for deep drawing has been manufactured. Steel B contains Cu, Sn, Ni, and Cr as playing elements and is a comparative example manufactured under normal hot rolling conditions, which is outside the conditions of the invention of the present application, and the r value is 1.
．． 52, and a steel plate for deep drawing has not been obtained. Steel C, D
, E are examples in which steel with almost the same composition and trumpet element content as Steel B was manufactured under the hot rolling conditions of the present invention, and Steel C is
In the embodiment of claim (1) where the winding temperature is 750°C, steel D is the embodiment of claim (2) where the heating temperature is 150°C, and steel E is the embodiment where the winding temperature is 760°C. This is an example in which both claims (1) and (2) are adopted in which the heating temperature is 1050°C, and excellent deep drawability is obtained in both cases. Steel F contains Cu, Sn, Ni, and Cr as playing elements, and B is used to improve secondary workability.
This is a comparative example manufactured under normal hot rolling conditions with the addition of
This is outside the conditions of the invention of the present application, and the r value is as low as 1.48, making it impossible to obtain a deep drawing steel plate for applications requiring secondary workability. Steel G is an embodiment of the present invention for producing a deep-drawing steel plate for applications requiring secondary workability, with the addition of B having approximately the same composition and trump element content as Steel F.
The winding temperature is 760℃ and the heating temperature is 1050℃.
This is an example in which both claims (1) and (2) are adopted, and excellent deep drawability is obtained. Steel H, I is P
Comparative Example Steel H manufactured under normal hot rolling conditions when producing a high strength steel sheet with excellent deep drawability by adding 100% C. and a coiling temperature of 750°C and a heating temperature of 1050°C. This is steel I of an example in which both (1) and (2) are adopted. Steel H does not meet the conditions of the present invention, and has a low r value of 1.42, making it impossible to obtain a high-strength steel plate with excellent deep drawability. Steel I is a high-strength steel plate with an r value of 1.75 and excellent deep drawability. Steel J was manufactured under the hot rolling conditions of the method of the present invention, but Cu, S
This is a comparative example in which the tramp element contains n, Ni, and Cr beyond the scope of the present invention, which is outside the conditions of the present invention, and the r value is as low as 1.55, making it impossible to obtain a steel plate for deep drawing. In addition, surface scratches have also occurred.
【００１２】0012
【発明の効果】以上に本発明について詳細に説明したが
、本発明によれば、Ｃｕ，Ｓｎ，Ｎｉ，Ｃｒ，がトラン
プエレメントとして残留する鋳片を用いても、深絞り性
が損なわれない深絞り用冷延鋼板の製造方法が可能とな
り、その工業的価値は大である。Effects of the Invention The present invention has been explained in detail above, and according to the present invention, deep drawability is not impaired even when a slab in which Cu, Sn, Ni, and Cr remain as tramp elements is used. A method for producing cold-rolled steel sheets for deep drawing has become possible, and its industrial value is great.
【図１】熱延巻き取り温度とｒ値の関係を示す図、[Fig. 1] A diagram showing the relationship between hot rolling winding temperature and r value,
【図
２】スラブの加熱温度とｒ値の関係を示す図である。FIG. 2 is a diagram showing the relationship between slab heating temperature and r value.
Claims (2)
の一部又は全量をスクラップで賄う方法でスラブを造り
、連続熱延、冷間圧延、再結晶焼鈍、調質圧延（以下Ｓ
．Ｐと記す）の工程を経て冷延鋼板を製造する方法にお
いて、Ｃ≦０．００８％，Ｓｉ≦０．６０％，Ｍｎ≦０
．８０％，Ｐ≦０．１２０％，Ｓ≦０．０３５％，ｓｏ
ｌＡｌ≦０．１００％，Ｎ≦０．００８０％，Ｔｉ：０
．０１０〜０．１０％，Ｂ≦０．００２０％，及びトラ
ンプエレメントとしてＣｕ：０．０５〜０．２０，Ｓｎ
：０．００５〜０．０２０，且つＣｕ（％）×Ｓｎ（％
）≦０．００２，Ｎｉ≦０．３％，Ｃｒ≦０．２％、残
部不可避的不純物及び鉄よりなる鋼片を、通常の方法で
加熱し連続熱延を行い６７０〜８００℃で巻き取り熱延
鋼帯とし、冷間圧延を行い、その後、連続焼鈍にて再結
晶焼鈍を行なった後Ｓ．Ｐを施すことを特徴とする深絞
り用冷延鋼板の製造方法。Claim 1: Slabs are made by a method in which a part or all of the iron source is provided by scrap during the steelmaking (melting, decarburization, and casting) process, and the slabs are continuously hot rolled, cold rolled, recrystallized annealed, and temper rolled ( Below S
．． In the method of manufacturing a cold rolled steel sheet through the process (denoted as P), C≦0.008%, Si≦0.60%, Mn≦0
．． 80%, P≦0.120%, S≦0.035%, so
lAl≦0.100%, N≦0.0080%, Ti:0
．． 010~0.10%, B≦0.0020%, and Cu as a playing card element: 0.05~0.20, Sn
:0.005~0.020, and Cu(%)×Sn(%
)≦0.002, Ni≦0.3%, Cr≦0.2%, the balance consisting of unavoidable impurities and iron is heated in a conventional manner, continuously hot rolled, and rolled up at 670 to 800°C. A hot-rolled steel strip was prepared, cold-rolled, and then recrystallized by continuous annealing. A method for producing a cold-rolled steel sheet for deep drawing, characterized by applying P.
０℃以下で行い、熱延後の巻き取り温度を８００℃以下
とすることを特徴とする請求項１記載の深絞り用冷延鋼
板の製造方法。[Claim 2] The slab heating temperature during hot rolling is 115
2. The method for producing a cold-rolled steel sheet for deep drawing according to claim 1, characterized in that the hot rolling is carried out at a temperature of 0°C or lower, and the coiling temperature after hot rolling is 800°C or lower.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17183691A JP2971192B2 (en) | 1991-06-18 | 1991-06-18 | Manufacturing method of cold-rolled steel sheet for deep drawing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17183691A JP2971192B2 (en) | 1991-06-18 | 1991-06-18 | Manufacturing method of cold-rolled steel sheet for deep drawing |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04371528A true JPH04371528A (en) | 1992-12-24 |
| JP2971192B2 JP2971192B2 (en) | 1999-11-02 |
Family
ID=15930660
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17183691A Expired - Fee Related JP2971192B2 (en) | 1991-06-18 | 1991-06-18 | Manufacturing method of cold-rolled steel sheet for deep drawing |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2971192B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5470529A (en) * | 1994-03-08 | 1995-11-28 | Sumitomo Metal Industries, Ltd. | High tensile strength steel sheet having improved formability |
| KR100514788B1 (en) * | 2000-12-05 | 2005-09-14 | 주식회사 포스코 | A method for manufacturing cold rolled steel sheets having superior surface quality |
-
1991
- 1991-06-18 JP JP17183691A patent/JP2971192B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5470529A (en) * | 1994-03-08 | 1995-11-28 | Sumitomo Metal Industries, Ltd. | High tensile strength steel sheet having improved formability |
| KR100514788B1 (en) * | 2000-12-05 | 2005-09-14 | 주식회사 포스코 | A method for manufacturing cold rolled steel sheets having superior surface quality |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2971192B2 (en) | 1999-11-02 |
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