JPH10183254A - Production of cold rolled steel sheet for deep drawing excellent in ridging resistance - Google Patents
Production of cold rolled steel sheet for deep drawing excellent in ridging resistanceInfo
- Publication number
- JPH10183254A JPH10183254A JP34693696A JP34693696A JPH10183254A JP H10183254 A JPH10183254 A JP H10183254A JP 34693696 A JP34693696 A JP 34693696A JP 34693696 A JP34693696 A JP 34693696A JP H10183254 A JPH10183254 A JP H10183254A
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、自動車等に使用さ
れる深絞り用冷延鋼板の製造方法に関し、とくに耐リジ
ング性に優れた深絞り用冷延鋼板の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a cold-rolled steel sheet for deep drawing used in automobiles and the like, and more particularly to a method for producing a cold-rolled steel sheet for deep drawing having excellent ridging resistance.
【0002】[0002]
【従来の技術】冷延鋼板の素材である熱延鋼板は、従
来、所定の組成を有する鋼スラブを1200℃以上の高温に
加熱・均熱したのち、粗圧延およびAr3 点以上の温度
範囲で圧延する仕上圧延を施して製造されていた。この
ようなスラブの高温加熱は、鋼の変形抵抗が高温のほう
が低いことを利用し、圧延動力の減少を図るほか、仕上
圧延終了時の鋼板温度をAr3 点以上の温度とするた
め、加熱後の粗圧延、仕上圧延段階での温度降下を補償
することにある。熱延鋼板の仕上温度がAr3 点以下と
なると、熱延鋼板の材質およびこれを素材とした冷延鋼
板の材質が悪くなる。一般的には、スラブ加熱温度を高
くとり、熱延仕上温度がAr3 点以上とすれば熱延鋼板
の結晶方位もランダム化し、これを素材とする冷延鋼板
も良好な材質が得られる。2. Description of the Related Art Conventionally, a hot-rolled steel sheet, which is a raw material of a cold-rolled steel sheet, is prepared by heating and equalizing a steel slab having a predetermined composition to a high temperature of 1200 ° C. or higher, followed by rough rolling and a temperature range of 3 points or more of Ar. It was manufactured by subjecting it to finish rolling. High temperature heating such a slab, since deformation resistance of the steel by utilizing the low towards the high temperature, to other to achieve reduction of the rolling force, the finish rolling end temperature steel temperature above Ar 3 point of the heating The purpose is to compensate for the temperature drop in the subsequent rough rolling and finish rolling stages. When the finishing temperature of the hot-rolled steel sheet is equal to or lower than the Ar 3 point, the material of the hot-rolled steel sheet and the material of the cold-rolled steel sheet using the same become poor. Generally, if the slab heating temperature is set high and the hot-rolling finishing temperature is set to three or more Ar points, the crystal orientation of the hot-rolled steel sheet is randomized, and a good cold-rolled steel sheet made of the same can be obtained.
【0003】しかしながら、スラブの高温加熱は、加熱
炉の炉寿命を短くし、そのため炉の補修費用等のコスト
増をもたらすうえ、スラブや鋼片表面に形成される酸化
膜が厚くなり、スケールの噛み込み等の表面欠陥の増加
や歩留り低下の一因ともなっていた。さらに、オーステ
ナイト(γ)域での圧延とするため、圧延ロールへの負
荷が大きくなり、ロール寿命が短くなるという問題もあ
った。[0003] However, high-temperature heating of the slab shortens the life of the heating furnace, thereby increasing costs such as repair costs of the furnace. In addition, the oxide film formed on the surface of the slab and steel slab becomes thicker, and the scale becomes smaller. This also contributed to an increase in surface defects such as biting and a decrease in yield. Furthermore, since the rolling is performed in the austenite (γ) region, there is a problem that the load on the rolling roll increases and the roll life is shortened.
【0004】このような問題に対し、例えば、特公昭57
-32696号公報には、熱間圧延をAr 3 点以下の低温で熱
間圧延する低炭素冷延鋼板の製造方法が開示されてい
る。この方法は、Ar3 点以下600 ℃以上のオーステナ
イト+フェライトの(γ+α)2相域で仕上圧下率を20
〜60%とする熱間圧延を行うことにより、Ar3 点以上
で仕上圧延された鋼板材質と比較して遜色のない低炭素
冷延鋼板を得ることを目的としている。しかし、Ar3
点以下で圧延を行うと、機械的性質、とくに延性、絞り
性に著しい劣化が生じること、さらにはリジングが発生
しやすいという問題が残されていた。[0004] In response to such a problem, for example,
Japanese Patent No. 32696 discloses that hot rolling is performed using Ar. ThreeHeat at low temperatures below the point
A method for producing a low-carbon cold-rolled steel sheet to be hot-rolled is disclosed.
You. This method uses ArThreeAustena below 600 ° C
20% finish reduction in (γ + α) two phase region
By performing hot rolling to % 60%, ArThreeAbove the point
Carbon that is comparable to the steel material finished and rolled in
The purpose is to obtain cold-rolled steel sheets. However, ArThree
If rolling is performed below the point, mechanical properties, especially ductility,
Remarkable deterioration of properties, and ridging
The problem that it was easy to do was left.
【0005】ここでいうリジングとは、製品の加工時に
生じる表面の凹凸欠陥であり、加工製品の最外側に使用
されることの多い深絞り用冷延鋼板では致命的な欠陥と
なる。また、特開平5-132718号公報には、C、N、S量
を限定し、さらにTiおよびNbのいずれか一方または双方
をC、N、S量との関連で制限した鋼にAr3 〜Ar 3
+100 ℃の温度域で合計圧下量が35%以上の圧延を行
い、その後γ→α変態時の平均冷却を10℃/sec以上で急
冷し、Ar3 点以下の温度域での合計圧下率が70%以上
とする圧延を行い、600 〜750 ℃で巻き取り、酸洗、冷
延、焼鈍を行うリジング発生のない深絞り用冷延鋼板の
製造方法が開示されている。しかし、この方法では、粗
圧延後に急冷処理を必要とし、工程上の複雑さ、冷却装
置の設置等コスト的にも能率的にも問題を残していた。[0005] Ridging as used herein refers to the time when a product is processed.
Surface defects that occur, used on the outermost surface of processed products
Critical defects are often encountered in cold-rolled steel sheets for deep drawing.
Become. Also, Japanese Patent Application Laid-Open No. Hei 5-132718 discloses that C, N, S
And further, one or both of Ti and Nb
Was restricted to steels in relation to the amounts of C, N and S.Three~ Ar Three
Rolling with a total reduction of 35% or more in a temperature range of + 100 ° C
After that, the average cooling during the γ → α transformation is suddenly increased at 10 ° C / sec or more.
Cool down, ArThreeThe total draft in the temperature range below the point is 70% or more
Rolled at 600-750 ° C, pickled and cooled
Cold drawn steel sheet for deep drawing without ridging
A manufacturing method is disclosed. However, with this method,
Requires quenching after rolling, complicating the process, cooling equipment
There were problems in terms of cost and efficiency, such as installation of equipment.
【0006】[0006]
【発明が解決しようとする課題】本発明は、上記した問
題を解決し、熱間圧延の生産性向上、表面欠陥の低減を
図り、耐リジング性に優れた冷延鋼板の製造方法を提供
することを目的とする。SUMMARY OF THE INVENTION The present invention solves the above-mentioned problems, improves the productivity of hot rolling, reduces surface defects, and provides a method for producing a cold-rolled steel sheet having excellent ridging resistance. The purpose is to:
【0007】[0007]
【課題を解決するための手段】本発明は、重量%で、
C:0.003 %以下、N:0.005 %以下、を含み、かつT
i:0.003 〜0.08%およびNb:0.002 〜0.05%のうちの
1種または2種を、次(1)式 Ti/48+Nb/93 ≧C/12 +N/14 …………(1) (ここで、Ti、Nb、C、N:重量%) を満足するように含有した鋼を連続鋳造鋳片としたの
ち、該鋳片を900 〜1100℃で加熱・均熱処理を施し、最
終粗スタンド圧下率が30%以上とする粗圧延と、圧延温
度がAr3 点以下800 ℃以上とする仕上圧延とを施して
熱延板とした後、該熱延板に冷間圧延、連続焼鈍を施す
ことを特徴とする耐リジング性に優れた深絞り用冷延鋼
板の製造方法である。SUMMARY OF THE INVENTION The present invention provides, in weight percent,
C: 0.003% or less, N: 0.005% or less, and T
One or two of i: 0.003 to 0.08% and Nb: 0.002 to 0.05% were obtained by the following formula (1): Ti / 48 + Nb / 93 ≧ C / 12 + N / 14 (1) , Ti, Nb, C, N:% by weight) to obtain a continuous cast slab, and then heat and soak the steel at 900 to 1100 ° C to obtain a final rough stand draft. Is subjected to a rough rolling of 30% or more and a finish rolling of a rolling temperature of 800 ° C. or more at an Ar 3 point or less to form a hot-rolled sheet, and then subject the cold-rolled and continuous annealing to the hot-rolled sheet. This is a method for producing a cold-rolled steel sheet for deep drawing having excellent ridging resistance.
【0008】また、本発明は、重量%で、C:0.003 %
以下、N:0.005 %以下、B:0.0003〜0.003 %を含
み、かつTi:0.003 〜0.08%およびNb:0.002 〜0.05%
のうちの1種または2種を、次(1)式 Ti/48+Nb/93 ≧C/12 +N/14 …………(1) (ここで、Ti、Nb、C、N:重量%) を満足するように含有した鋼を連続鋳造鋳片としたの
ち、該鋳片を900 〜1100℃で加熱・均熱処理を施し、最
終粗スタンド圧下率が30%以上とする粗圧延と、圧延温
度がAr3 点以下800 ℃以上とする仕上圧延とを施して
熱延板とした後、該熱延板に冷間圧延、連続焼鈍を行う
ことを特徴とする耐リジング性に優れた深絞り用冷延鋼
板の製造方法である。[0008] The present invention also relates to a method of the present invention wherein C: 0.003% by weight.
Below, N: 0.005% or less, B: 0.0003 to 0.003%, Ti: 0.003 to 0.08% and Nb: 0.002 to 0.05%
One or two of the above are represented by the following formula (1): Ti / 48 + Nb / 93 ≧ C / 12 + N / 14 (1) (where Ti, Nb, C, N: wt%) After making the steel satisfactorily contained into a continuous cast slab, the slab is subjected to heating and soaking at 900 to 1100 ° C, and the rough rolling is performed so that the final rough stand draft is 30% or more. Ar 3 points or less and finish rolling to 800 ° C. or more to form a hot-rolled sheet, and then subject the cold-rolled sheet to cold rolling and continuous annealing. This is a method for producing a rolled steel sheet.
【0009】[0009]
【発明の実施の形態】以下に、本発明における限定理由
について説明する。本発明では、連続鋳造鋳片のCは0.
003 %以下、Nは0.005 %以下とする。連続焼鈍を実施
する本発明では、C、N量が上記値を超えると、非時効
性、深絞り性が劣化する。DESCRIPTION OF THE PREFERRED EMBODIMENTS The reasons for limitation in the present invention will be described below. In the present invention, C of the continuous cast slab is 0.
003% or less and N should be 0.005% or less. In the present invention in which continuous annealing is performed, when the C and N contents exceed the above values, the non-aging property and the deep drawability deteriorate.
【0010】また、本発明では、上記組成に加えて、T
i、Nbのうちの1種または2種を添加する。Ti、Nbは固
溶C、固溶Nを固定し、安定な炭化物あるいは窒化物と
して析出させ、深絞り性に有利な集合組織を形成させる
ために添加する。添加するTi、Nb量は、それぞれ0.003
〜0.08%、0.003 〜0.05%の範囲とする。0.003 %未満
では、上記した効果が期待できない。一方Tiが0.08%、
Nbが0.05%を超えて添加しても、添加量に比例した機械
的性質の向上は望めない。In the present invention, in addition to the above composition, T
One or two of i and Nb are added. Ti and Nb are added to fix solid solution C and solid solution N, precipitate as stable carbide or nitride, and form a texture advantageous for deep drawability. The amounts of Ti and Nb to be added are 0.003, respectively.
-0.08%, 0.003-0.05%. If it is less than 0.003%, the above effects cannot be expected. On the other hand, Ti is 0.08%,
Even if Nb is added in excess of 0.05%, improvement in mechanical properties in proportion to the added amount cannot be expected.
【0011】さらに、Ti、Nbは、上記範囲内でかつC、
N量と関連して(1)式を満足するように調整する。
(1)式、 Ti/48+Nb/93 ≧C/12 +N/14 (ここで、
Ti、Nb、C、N:重量%)が満足されない場合には、固
溶C、固溶Nを固定するためのTi、Nb量が不足し、非時
効性、深絞り性が劣化する。上記した成分以外に、Mnは
0.20%以下、Siは 0.1%以下、Pは0.03%以下、Sは
0.015%以下とするのが好ましい。その他残部は実質的
にFeである。Further, Ti and Nb are within the above range and C,
Adjustment is made so as to satisfy the expression (1) in relation to the N amount.
Equation (1), Ti / 48 + Nb / 93 ≧ C / 12 + N / 14 (where,
If Ti, Nb, C, and N are not satisfied, the amounts of Ti and Nb for fixing solid solution C and solid solution N are insufficient, and the non-aging property and the deep drawability deteriorate. In addition to the above components, Mn
0.20% or less, Si is 0.1% or less, P is 0.03% or less, S is
It is preferably set to 0.015% or less. The other balance is substantially Fe.
【0012】上記した組成の鋳片は900 〜1100℃で加熱
・均熱処理を施される。本発明では、鋳片の加熱均熱処
理は、加熱・均熱中に生じる析出物を粗大化して延性、
絞り性を向上させるために行う。加熱温度が1100℃を超
えると析出物が微細化して延性、絞り性の向上が得られ
ない。一方、900 ℃未満では、熱量の節減効果は著しい
が、鋼の変形抵抗が急激に増加するため、圧延が困難と
なる。The slab having the composition described above is subjected to heating and soaking at 900 to 1100 ° C. In the present invention, the heat soaking heat treatment of the slab, ductility by coarsening the precipitates generated during heating and soaking,
This is performed to improve drawability. If the heating temperature exceeds 1100 ° C., the precipitates become finer, and improvement in ductility and drawability cannot be obtained. On the other hand, when the temperature is lower than 900 ° C., the effect of reducing the amount of heat is remarkable, but the deformation resistance of the steel sharply increases, so that the rolling becomes difficult.
【0013】加熱均熱された鋳片は、熱間圧延により熱
延板とされる。熱間圧延は、粗圧延、仕上圧延の2段階
で構成される。リジングは、金属学的には、熱間圧延後
に、加工−再結晶過程を経ても容易に分割されない結晶
方位群、例えば、{100 }方位粒群が圧延方向に伸ばさ
れて残留することに起因するものである。本発明者ら
は、リジングは粗圧延後の再結晶に続く粒成長により顕
著となり、粗圧延後の再結晶に続く粒成長を抑えればリ
ジングの発生を防止できることを新たに知見した。そこ
で、本発明では、粗圧延の最終スタンド圧下率をを30%
以上とする。これにより、再結晶後の粒成長が抑制さ
れ、リジングの発生を防止できる。30%未満では、上記
した効果が期待できない。The slab that has been heated and soaked is formed into a hot-rolled sheet by hot rolling. Hot rolling is composed of two stages of rough rolling and finish rolling. Ridging is metallurgically caused by the fact that after hot rolling, a group of crystal orientations that are not easily divided even after a working-recrystallization process, for example, {100} orientation grains are stretched in the rolling direction and remain. Is what you do. The present inventors have newly found that the ridging is remarkable due to the grain growth following the recrystallization after the rough rolling, and the occurrence of the ridging can be prevented by suppressing the grain growth following the recrystallization after the rough rolling. Therefore, in the present invention, the final stand draft of the rough rolling is reduced by 30%.
Above. Thereby, grain growth after recrystallization is suppressed, and generation of ridging can be prevented. If it is less than 30%, the above effects cannot be expected.
【0014】なお、Bを含有する場合は35%以上とする
のが好ましい。また、粗圧延最終スタンド圧下率の上限
は、主に、鋼種と圧延機の能力との関係により決定され
るがこの鋼種では40%程度である。また、粗圧延は、A
r3 点以上で終了するのがリジング発生防止の点から好
ましい。When B is contained, the content is preferably at least 35%. The upper limit of the rolling reduction of the final stand in the rough rolling is determined mainly by the relationship between the steel type and the capacity of the rolling mill, and is about 40% for this steel type. In addition, rough rolling
to end at r 3 points or more are preferable from the viewpoint of ridging prevention.
【0015】仕上圧延は、Ar3 点以下800 ℃以上のα
域圧延とする。α域圧延とすることにより、同一温度で
γ域で圧延する場合にくらべ、変形抵抗が低く圧延動力
が少なくてよく、経済的となる。しかし、圧延温度が低
くなり800 ℃未満となると、仕上圧延後の再結晶が困難
となり、目標とする機械的性質が確保できない。なお、
Bを含有する場合は、熱延後の再結晶性確保の点から82
0 ℃以上とするのが好ましい。In the finish rolling, α of 800 ° C. or more at an Ar 3 point or less
Zone rolling. By using the α region rolling, the deformation resistance is low and the rolling power can be reduced, which is more economical than when rolling is performed in the γ region at the same temperature. However, when the rolling temperature is lowered to less than 800 ° C., recrystallization after finish rolling becomes difficult, and the target mechanical properties cannot be secured. In addition,
When B is contained, it is necessary to ensure recrystallization after hot rolling.
The temperature is preferably set to 0 ° C. or higher.
【0016】熱延板は、コイルに巻き取られたのち、酸
洗を施される。酸洗は、熱延板の表面スケールを除去す
るために行われるが、酸洗液、処理条件は通常公知の方
法でよい。本発明の方法で処理された熱延板は酸化層の
厚みは薄く、酸洗性は良好で、酸洗によるロスは少な
い。熱延板は、酸洗後、所定の板厚とする冷間圧延を施
され、ついで連続焼鈍を施され製品とされる。The hot rolled sheet is pickled after being wound around a coil. The pickling is performed to remove the surface scale of the hot-rolled sheet, and the pickling solution and the processing conditions may be generally known methods. The hot rolled sheet treated by the method of the present invention has a thin oxide layer, good pickling properties, and little loss due to pickling. The hot-rolled sheet is subjected to cold rolling to a predetermined thickness after pickling, and then to continuous annealing to obtain a product.
【0017】冷間圧延は、所定の製品厚となればよく、
本発明ではとくに冷延条件を規定しないが、焼鈍後の特
性をよくするためには冷延圧下率は60%以上とするのが
望ましい。冷延後の連続焼鈍は、600 ℃〜900 ℃の温度
範囲で行うのが望ましい。本発明の冷延鋼板は、深絞り
用を主目的としているが、亜鉛めっき性、錫めっき性、
ほうろう性等の表面処理性にも優れ、亜鉛めっき、錫め
っき、ほうろう等の表面処理を施す各種表面処理原板と
して適用できることは言うまでもない。In the cold rolling, a predetermined product thickness may be obtained.
In the present invention, the conditions of the cold rolling are not particularly specified. However, in order to improve the properties after annealing, it is desirable that the rolling reduction of the cold rolling is 60% or more. The continuous annealing after the cold rolling is desirably performed in a temperature range of 600 ° C to 900 ° C. The cold-rolled steel sheet of the present invention is mainly used for deep drawing, but has a zinc plating property, a tin plating property,
It is needless to say that it has excellent surface treatment properties such as enamelness and can be applied as various surface-treated original sheets subjected to surface treatment such as zinc plating, tin plating, and enamel.
【0018】[0018]
【実施例】表1に示す組成の鋼を、転炉により溶製し、
連続鋳造によりスラブとしたのち、表2、表3に示す圧
延条件で熱間圧延を施し熱延板とした。これら熱延板を
塩酸液で酸洗し、表2、表3に示す圧延条件で冷間圧延
を行い、 0.7〜 1.2mm厚の冷延板とした。ついで、これ
ら冷延板を、表2、表3に示す連続焼鈍条件で焼鈍し
た。EXAMPLES Steel having the composition shown in Table 1 was melted by a converter,
After a slab was formed by continuous casting, hot rolling was performed under the rolling conditions shown in Tables 2 and 3 to obtain a hot-rolled sheet. These hot-rolled sheets were pickled with a hydrochloric acid solution and cold-rolled under the rolling conditions shown in Tables 2 and 3 to obtain cold-rolled sheets having a thickness of 0.7 to 1.2 mm. Next, these cold-rolled sheets were annealed under continuous annealing conditions shown in Tables 2 and 3.
【0019】[0019]
【表1】 [Table 1]
【0020】これら焼鈍板について、JIS 5号試験片を
用いて引張特性を調査した。また、リジング性は、これ
ら焼鈍板の圧延方向から切り出したJIS 5号試験片に、
15%の引張予歪を付加したのち、表面の凹凸を目視で評
価した。評価は、1を良、5を劣とし1〜5の5段階評
価とした。これらの結果を表2、表3に示す。評価1、
2におけるジリング発生は、実用上問題のない程度であ
る。The tensile properties of these annealed sheets were examined using JIS No. 5 test pieces. In addition, the ridging property was measured on JIS No. 5 test pieces cut from the rolling direction of these annealed sheets.
After a tensile prestrain of 15% was added, the surface irregularities were visually evaluated. In the evaluation, 1 was evaluated as good and 5 was evaluated as inferior and 1 to 5 was evaluated. Tables 2 and 3 show these results. Evaluation 1,
The occurrence of gilding in No. 2 is of such a degree that there is no practical problem.
【0021】[0021]
【表2】 [Table 2]
【0022】[0022]
【表3】 [Table 3]
【0023】表2、表3から、本発明の範囲で製造され
た本発明例の鋼板は、伸び値は48%以上、r値は1.9 以
上と引張特性、絞り性はすぐれ、またリジング性の評価
は1または2であり、リジング発生は実用上問題のない
程度となっている。これに対し、本発明の範囲を外れる
比較例の鋼板では、伸び値、r値が低いか、リジングが
発生している。From Tables 2 and 3, the steel sheet of the present invention manufactured within the scope of the present invention has an elongation value of 48% or more, an r value of 1.9 or more, excellent tensile properties, drawability, and ridging properties. The evaluation was 1 or 2, and the occurrence of ridging was of a practically acceptable level. On the other hand, in the steel sheet of the comparative example out of the range of the present invention, the elongation value and the r value are low, or ridging occurs.
【0024】仕上圧延温度が低い試験No.5、試験No.16
では、r値が低い。加熱温度が高い試験No.7、試験No.1
8 では、リジングが発生している。粗圧延最終スタンド
圧下率が低い試験No.9、試験No.20 では、r 値が低くま
たリジングが発生している。鋼組成が本発明の範囲を外
れた試験No.10 、No.11 、No.21 、No.22 では、r値が
低い。Test No. 5 and Test No. 16 with low finishing rolling temperature
Has a low r value. Test No. 7, Test No. 1 with high heating temperature
In 8, ridging has occurred. In Test No. 9 and Test No. 20, where the rolling reduction of the final stand in the rough rolling was low, the r value was low and ridging occurred. In tests No. 10, No. 11, No. 21 and No. 22 in which the steel composition was out of the range of the present invention, the r value was low.
【0025】[0025]
【発明の効果】本発明によれば、複雑な工程や特別な装
置を必要としないため、熱間圧延の生産性が向上し耐リ
ジング性に優れた冷延鋼板が安価に製造でき、しかも従
来より低温で加熱するため、表面スケールの噛み込み等
の表面欠陥が低減するという産業上格段の効果が期待で
きる。According to the present invention, since a complicated process and special equipment are not required, a cold-rolled steel sheet having improved hot rolling productivity and excellent ridging resistance can be manufactured at low cost. Since the heating is performed at a lower temperature, an industrially remarkable effect of reducing surface defects such as biting of the surface scale can be expected.
Claims (2)
よびNb:0.002 〜0.05%のうちの1種または2種を、下
記(1)式を満足するように含有した鋼を連続鋳造鋳片
としたのち、該鋳片を900 〜1100℃で加熱・均熱処理を
施し、最終粗スタンド圧下率が30%以上とする粗圧延
と、圧延温度がAr3 点以下800 ℃以上とする仕上圧延
とを施して熱延板とした後、該熱延板に冷間圧延、連続
焼鈍を施すことを特徴とする耐リジング性に優れた深絞
り用冷延鋼板の製造方法。 記 Ti/48+Nb/93 ≧C/12 +N/14 …………(1) ここで、Ti、Nb、C、N:重量%1. The method according to claim 1, wherein the content of C is 0.003% or less, N is 0.005% or less, and one or two of Ti: 0.003 to 0.08% and Nb: 0.002 to 0.05% are represented by the following ( 1) After making a steel containing the steel satisfying the formula into a continuous cast slab, the slab is heated and soaked at 900 to 1100 ° C., and the rough rolling is performed to reduce the final rough stand rolling reduction to 30% or more. A hot-rolled sheet obtained by subjecting a hot-rolled sheet to finish rolling in which the rolling temperature is Ar 3 points or less and 800 ° C. or higher, and then subjecting the hot-rolled sheet to cold rolling and continuous annealing, which is excellent in ridging resistance. Manufacturing method of cold-rolled steel sheet for deep drawing. Note Ti / 48 + Nb / 93 ≧ C / 12 + N / 14 (1) where, Ti, Nb, C, N: wt%
%およびNb:0.002 〜0.05%のうちの1種または2種
を、下記(1)式を満足するように含有した鋼を連続鋳
造鋳片としたのち、該鋳片を900 〜1100℃で加熱・均熱
処理を施し、最終粗スタンド圧下率が30%以上とする粗
圧延と、圧延温度がAr3 点以下800 ℃以上とする仕上
圧延とを施して熱延板とした後、該熱延板に冷間圧延、
連続焼鈍を行うことを特徴とする耐リジング性に優れた
深絞り用冷延鋼板の製造方法。 記 Ti/48+Nb/93 ≧C/12 +N/14 …………(1) ここで、Ti、Nb、C、N:重量%2. The composition according to claim 2, wherein C: 0.003% or less, N: 0.005% or less, B: 0.0003 to 0.003%, and Ti: 0.003 to 0.08% by weight.
% And Nb: A continuous cast slab containing steel containing one or two of 0.002 to 0.05% so as to satisfy the following formula (1), and then heating the slab at 900 to 1100 ° C. After performing soaking heat treatment and performing rough rolling in which the final rough stand draft is 30% or more and finish rolling in which the rolling temperature is 800 ° C. or more at three points or less, a hot rolled sheet is obtained. Cold rolling,
A method for producing a cold-rolled steel sheet for deep drawing excellent in ridging resistance, characterized by performing continuous annealing. Note Ti / 48 + Nb / 93 ≧ C / 12 + N / 14 (1) where, Ti, Nb, C, N: wt%
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP34693696A JPH10183254A (en) | 1996-12-26 | 1996-12-26 | Production of cold rolled steel sheet for deep drawing excellent in ridging resistance |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP34693696A JPH10183254A (en) | 1996-12-26 | 1996-12-26 | Production of cold rolled steel sheet for deep drawing excellent in ridging resistance |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH10183254A true JPH10183254A (en) | 1998-07-14 |
Family
ID=18386828
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP34693696A Pending JPH10183254A (en) | 1996-12-26 | 1996-12-26 | Production of cold rolled steel sheet for deep drawing excellent in ridging resistance |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH10183254A (en) |
-
1996
- 1996-12-26 JP JP34693696A patent/JPH10183254A/en active Pending
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