JP2581887B2 - High strength cold rolled steel sheet excellent in cold workability and method for producing the same - Google Patents
High strength cold rolled steel sheet excellent in cold workability and method for producing the sameInfo
- Publication number
- JP2581887B2 JP2581887B2 JP2307293A JP2307293A JP2581887B2 JP 2581887 B2 JP2581887 B2 JP 2581887B2 JP 2307293 A JP2307293 A JP 2307293A JP 2307293 A JP2307293 A JP 2307293A JP 2581887 B2 JP2581887 B2 JP 2581887B2
- Authority
- JP
- Japan
- Prior art keywords
- cold
- steel sheet
- rolled
- rolled steel
- steel
- 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.)
- Expired - Fee Related
Links
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)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、近年とみに増加しつつ
ある自動車スクラップなどから発生するくず鉄の再利用
をはかるため、電気炉によるくず鉄の再溶解材を対象
に、混入した種々の元素を調整し必要な元素を添加し
た、とりわけ高い〔Ｎ〕を含有しながらも冷間成形性に
優れ、かつ高強度を有する高強度冷延鋼板に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention adjusts various elements mixed with a remelted material of scrap iron by an electric furnace in order to reuse scrap iron generated from automobile scraps and the like which is increasing rapidly in recent years. The present invention also relates to a high-strength cold-rolled steel sheet having a high formability and a high strength while containing particularly high [N] to which necessary elements are added.
【０００２】[0002]
【従来の技術】近年、自動車用冷延鋼板の品質および製
造技術が著しく進展し、特に冷間での深絞り加工性を表
わすｒ値（ランクフォード値）は２．０以上にも達する
ようになった。このような高性能を得る技術として、た
とえば特公昭４４−１８０６６号公報にはＣ量を０．０
０１〜０．０２０％、Ｏ量を０．０１５％まで低減した
上で、Ｔｉを０．０２〜０．５％添加して〔Ｃ〕を固定
安定化する技術手法を開示している。また特公平３−５
４１８６号公報にはＣ量，Ｎ量を共に０．００５０％以
下に低減し、かつＴｉ，Ｎｂを添加してＣ，Ｎを固定す
る方法、その他特公昭５３−１２８８９号公報、特公平
３−５６３０１号公報にもＣおよびＮを極力低減しそれ
らの固定にＴｉ，ＮｂのほかＢを添加する技術などが開
示されている。これらのほかも含めて従来技術はいずれ
もＣ，Ｎを可能な限り低減することを共通の技術思想と
して、非時効性かつ冷間プレス加工性に優れた冷延鋼板
を製造する方法を提示している。2. Description of the Related Art In recent years, the quality and manufacturing technology of cold rolled steel sheets for automobiles have been remarkably advanced, and in particular, the r value (Rankford value) representing deep drawing workability in the cold has reached 2.0 or more. became. As a technique for obtaining such a high performance, for example, Japanese Patent Publication No. 44-18066 discloses that the C content is 0.0
Disclosed is a technical method of fixing and stabilizing [C] by adding 0.02 to 0.5% of Ti after reducing the O content to 0.01 to 0.020% and O content to 0.015%. In addition, 3-5
Japanese Patent No. 4186 discloses a method in which both C and N contents are reduced to 0.0050% or less, and C and N are fixed by adding Ti and Nb. No. 56301 also discloses a technique of reducing C and N as much as possible and adding B in addition to Ti and Nb for fixing them. In addition to these, all of the prior arts have a common technical idea of reducing C and N as much as possible, and present a method of manufacturing a cold-rolled steel sheet having excellent non-aging properties and excellent cold press workability. ing.
【０００３】ところで、今日、市中に堆積しつつある鉄
のスクラップの再利用が時代の重要課題となっている
が、転炉ではスクラップの大量利用に限界があり、この
ためにスクラップを電気炉でアーク溶解する方法を採用
すると鋼中のＮは０．００５％以上の高いレベルになっ
てしまい、これを低減するには真空脱ガスなどの方法を
用いねばならず、採算上から上記の従来技術手法の原材
料には適用できず、電気炉鋼から、すなわち市中スクラ
ップを多量に再利用した鋼から加工性の優れた冷延鋼板
が製造されていないのが現状である。[0003] By the way, today, the reuse of iron scrap that is accumulating in the city has become an important issue in the era. However, there is a limit to the large amount of scrap that can be used in converters. If the method of arc melting is adopted, N in steel will be at a high level of 0.005% or more. To reduce this, a method such as vacuum degassing must be used. It cannot be applied to the raw materials of the technical methods, and at present, cold rolled steel sheets with excellent workability are not manufactured from electric furnace steel, that is, steel made by reusing a large amount of commercial scrap.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、電気炉溶解
でのこのような問題を解決し、スクラップの再利用対象
を拡大しようとするものである。すなわち、今日、市中
に堆積しつつある鉄のスクラップを再利用し、高Ｎ鋼で
あっても非時効性かつ冷間プレス加工性に優れた冷延鋼
板を製造する方法を提供することを目的とする。SUMMARY OF THE INVENTION The present invention relates to an electric furnace melting method.
In order to solve such a problem in the above, the scrap recycling target is expanded. That is, it is an object of the present invention to provide a method of manufacturing a cold-rolled steel sheet that is non-ageing and excellent in cold press workability even with high-N steel by recycling iron scrap that is accumulating in the market today. Aim.
【０００５】[0005]
【課題を解決するための手段】冷間プレス加工性を表す
特性として深絞り性と張り出し性をとり、それぞれｒ値
およびエリクセン（Ｅｒ）値で示すと、それらは引張り
試験における全伸び値と相関があり、特にｒ値は一様伸
びと強い相関を持つことが知られている。本発明者ら
は、上記の目的を達成すべく、鋼の化学成分、結晶組織
と得られる機械的性質、材質との関係などを詳細に調査
研究するうち、〔Ｎ〕含有量の高い鋼に適量のＴｉを添
加した鋼の一様伸び／全伸びの比は、低Ｎ鋼のそれより
も大きく、しかも同じ強度であれば全伸びも大きいこと
を知見した。Means for Solving the Problems Deep drawability and stretchability are taken as characteristics representing cold press workability, and when expressed by r value and Erichsen (Er) value, respectively, they are correlated with the total elongation value in a tensile test. In particular, it is known that the r value has a strong correlation with the uniform elongation. In order to achieve the above object, the present inventors conducted detailed research on the chemical composition of steel, the crystal structure and the obtained mechanical properties, the relationship between the materials, and the like. It has been found that the ratio of uniform elongation / total elongation of the steel to which an appropriate amount of Ti is added is larger than that of the low-N steel, and that the total elongation is large at the same strength.
【０００６】本発明はこれらの知見に基づくものであっ
て、従来ｒ値に有害とされるＮを多量に含有することを
前提に、鋼成分と製造工程とを特定することにより構成
したものである。すなわち、電気炉で溶製した高Ｎ鋼で
あって、重量比で、 Ｃ ：０．００５〜０．１０％、 Ｓｉ≦０．５％、 Ｍｎ≦１．０％、 Ｐ ≦０．１５％、 Ｓ ≦０．０３５％、 酸可溶Ａｌ：０．００５〜０．１０％、 Ｔｉ：０．００３〜０．０５１３％未満、 Ｂ ：０．０００１〜０．００５０％、 Ｎ ：０．００５５〜０．０１５０％、かつ Ｔｉ＜３．４２Ｎを基本成分とし、 あるいは必要に応じてこれに加えて、 Ｎｂ≦０．１％、 Ｖ ≦０．２％、 Ｚｒ≦０．１５％、 Ｃｕ≦０．３％、 Ｎｉ≦０．７％、 Ｃｒ≦０．２％、 Ｍｏ≦０．１％、 Ｃａ≦０．００７％、 ＲＥＭ≦０．０５％、のいずれか１種または２種以上を
含み残部Ｆｅおよび不可避的元素よりなることを特徴と
する冷間加工性に優れた高強度冷延鋼板であり、また、
上記各成分を含有する鋼板を得るために、電気炉で溶製
して製造した鋼片を、連続熱間圧延して５００℃以上の
温度で巻取り、冷間圧延して冷延鋼板とし、次いでこの
冷延鋼板を箱型焼鈍あるいは連続焼鈍方式により再結晶
焼鈍および必要に応じて過時効処理することによって製
造することを特徴とする冷間加工性に優れた高強度冷延
鋼板である。The present invention is based on these findings and is based on the premise that a large amount of N, which is conventionally detrimental to the r value, is specified by specifying the steel composition and the production process. is there. In other words, with high N steel melted in an electric furnace
C: 0.005 to 0.10%, Si ≦ 0.5%, Mn ≦ 1.0%, P ≦ 0.15%, S ≦ 0.035%, acid soluble Al by weight ratio : 0.005 to 0.10%, Ti: 0.003 to less than 0.0513%, B: 0.0001 to 0.0050%, N: 0.0055 to 0.0150% , and Ti <3.42N As a basic component, or if necessary, in addition, Nb ≦ 0.1%, V ≦ 0.2%, Zr ≦ 0.15%, Cu ≦ 0.3%, Ni ≦ 0.7%, Cr ≦ 0.2%, Mo ≦ 0.1%, Ca ≦ 0.007%, REM ≦ 0.05%, and one or more of the following, with the balance being Fe and unavoidable elements It is a high-strength cold-rolled steel sheet with excellent cold workability,
Melting in an electric furnace to obtain a steel sheet containing each of the above components
The steel slab manufactured as described above is continuously hot-rolled, wound at a temperature of 500 ° C. or more, cold-rolled into a cold-rolled steel sheet, and then the cold-rolled steel sheet is recrystallized by box annealing or continuous annealing. It is a high-strength cold-rolled steel sheet excellent in cold workability, characterized by being manufactured by overaging as required.
【０００７】[0007]
【作用】以下、本発明について詳細に説明する。本発明
においては先ず、鋼成分の限定理由について述べる。Ｃ
は、鋼の強度を上昇させ、ｒ値を低下させ、冷間加工性
を低下させるのでその上限を０．１０％とする。また、
精錬によってＣを減少させると溶鋼中のＯが増大しやは
り冷間加工性を低下させるので好ましくなく、強度確保
の上からも下限を０．００５％とする。さらに、３５kg
f/mm2 以上の引張強度を有効に付与するためには、０．
００８％以上とすることが好ましい。Hereinafter, the present invention will be described in detail. In the present invention, first, the reasons for limiting the steel components will be described. C
Increases the strength of the steel, lowers the r value, and lowers the cold workability. Therefore, the upper limit is set to 0.10%. Also,
If C is reduced by refining, O in the molten steel increases, which also lowers the cold workability, which is not preferable, and the lower limit is made 0.005% from the viewpoint of securing strength. In addition, 35kg
In order to effectively provide a tensile strength of f / mm 2 or more, it is necessary to set the tensile strength to 0.1%.
It is preferably at least 008%.
【０００８】Ｓｉ，Ｍｎは、冷間加工性をそれほど低下
させずに強度を上昇させるので有用であるが、過度の添
加は硬化を招きｒ値を低下させるので、上限をそれぞれ
０．５％、１．０％とする。Ｐは、高強度化、ｒ値の向
上に有用であるが、含有量が０．１５％を超えると溶接
性の低下を招くので０．１５％の範囲に限定する。Ｓ
は、鋼中含有量が増すと熱間圧延時に赤熱脆性を生じ、
割れを発生させる恐れがあるので０．０３５％以下の範
囲に限定する。[0008] Si and Mn are useful because they increase the strength without significantly lowering the cold workability, but excessive addition causes hardening and lowers the r-value. 1.0%. P is useful for increasing the strength and improving the r-value. However, if the content exceeds 0.15%, the weldability is reduced. Therefore, the content of P is limited to the range of 0.15%. S
Causes red hot embrittlement during hot rolling when the content in steel increases,
Since cracks may occur, the range is limited to 0.035% or less.
【０００９】Ｎは、一般にＣと同様時効性を増し、ｒ値
や延性を低下させ冷間加工性の劣化を招く元素であり、
従って冷延鋼板の冷間加工性の向上を目的とする総ての
先行技術ができる限りＮを低減することを基本思想とし
ている。しかしながら鉄のスクラップの再利用をはか
り、さらには電気炉での精錬を生産効率よく、かつ経済
効果に見合うよう行うためにはＮ含有量の極端な低減は
不利である。そのために本発明においては０．００５５
％以上含有させる。操業上有利にするためには０．００
８０％以上とするのが好ましい。しかし、あまり多量に
含有させると前記特性の劣化が生じるので０．０１５０
％以下とする。N is an element that generally increases aging properties like C, reduces r value and ductility, and causes deterioration of cold workability.
Therefore, the basic idea is to reduce N as much as possible in all prior arts aiming at improving the cold workability of cold rolled steel sheets. However, extreme reduction of the N content is disadvantageous in order to reuse iron scrap and to perform refining in an electric furnace with good production efficiency and economic effects. Therefore, in the present invention, 0.0055
% Or more. 0.00 for operational advantage
It is preferably at least 80%. However, if it is contained in an excessively large amount, the above-mentioned characteristics are deteriorated.
% Or less.
【００１０】Ｔｉは、溶鋼中でＮと結合しＴｉＮを形
成、固溶Ｎを低減し、ｒ値を向上させる。しかしなが
ら、本発明が対象とする高Ｎ鋼となる溶鋼の場合には、
含有Ｎ当量のＴｉを添加すると鋼中に介在物として残存
するＴｉＮの個数が著しく増すほか、ＴｉＮそのものも
粗大化し、固溶Ｎは低減してもかえってｒ値を低下させ
てしまう。この問題を解決する手段として詳細な研究の
結果、溶解凝固過程で鋼中Ｎの全部を固定するのではな
く、溶解凝固過程、熱間圧延〜巻取り過程、焼鈍過程の
３過程に分けて鋼中Ｎを固定する方法が最適であること
を見いだした。すなわち溶解凝固過程では主としてＴ
ｉ、圧延過程では主としてＢ、焼鈍過程では主としてＡ
ｌにより鋼中Ｎを固定する方法である。そのための各元
素の最適量は、Ｔｉは０．００３〜０．０５１３％未満
で、Ｎ当量以下、すなわちＴｉ＜３．４２×Ｎ％とし、
Ｂは０．０００１〜０．００５０％、酸可溶Ａｌは０．
００５〜０．１０％とする。なお、凝固速度が小さいと
ＴｉＮが粗大化してｒ値を低下させるので鋼片厚みが２
５０mm以下の連続鋳造を採用するのが好ましい。[0010] Ti combines with N in molten steel to form TiN, thereby reducing solid solution N and improving the r value. However, in the case of molten steel that is a high N steel targeted by the present invention,
Addition of Ti equivalent to the content of N causes the number of TiN remaining as inclusions in the steel to significantly increase, and also increases the coarseness of TiN itself, thereby lowering the r value even though solid solution N is reduced. As a means of solving this problem, as a result of detailed research, instead of fixing all of the N in the steel during the melt-solidification process, the steel was divided into three processes: melt-solidification process, hot rolling to winding process, and annealing process. It has been found that the method for fixing the medium N is optimal. That is, in the melting and coagulation process, T
i, mainly B in the rolling process and A in the annealing process
This is a method of fixing N in steel by l. The optimal amount of each element for that is 0.003 to less than 0.0513% of Ti.
And N or less, that is, Ti <3.42 × N% ,
B is 0.0001 to 0.0050%, acid-soluble Al is 0.
And 005 to 0.10 percent. If the solidification rate is low, TiN becomes coarse and the r-value is reduced.
It is preferable to employ continuous casting of 50 mm or less.
【００１１】以上の元素のほかに、必要に応じてさらに
以下の諸元素を添加することができる。Ｚｒは、Ｔｉの
一部として置換が可能でその場合、０．１５％を上限と
して添加する。Ｎｂ，Ｖは、Ａｌの一部として置換が可
能でその場合、それぞれ０．１％，０．２％を上限とし
て添加する。Ｃｕ，Ｎｉはｒ値を低下させない範囲で耐
食性を考慮する場合、それぞれ０．３％，０．７％を上
限として添加する。Ｃｒ，Ｍｏはｒ値を低下させない範
囲で強度の向上を考慮する場合、それぞれ０．２％，
０．１％を上限として添加する。Ｃａ，ＲＥＭは、焼付
硬化（ＢＨ）性に不利といわれる遊離Ｓを固定するため
に、必要に応じてそれぞれ０．００７％，０．０５％を
上限として添加する。In addition to the above-mentioned elements, the following various elements can be further added as required. Zr can be substituted as part of Ti, and in that case, 0.15% is added as an upper limit. Nb and V can be substituted as a part of Al. In this case, 0.1% and 0.2% are added as upper limits. When considering corrosion resistance within a range that does not decrease the r value, Cu and Ni are added with 0.3% and 0.7% as upper limits, respectively. Cr and Mo are 0.2% and 0.2%, respectively, when considering the improvement in strength within a range that does not reduce the r value.
Add 0.1% as the upper limit. Ca and REM are added as necessary in an upper limit of 0.007% and 0.05%, respectively, in order to fix free S which is disadvantageous to bake hardening (BH) properties.
【００１２】このような成分を含む本発明の冷延鋼板は
以下の方法で製造する。すなわち、電気炉スクラップを
主たる鉄原材料として溶製し、上記のような成分範囲に
調整した高Ｎ鋼を、造塊・分塊あるいは連続鋳造して鋼
片とした後、熱片直送して、あるいは温片または冷片を
１０００〜１３００℃に再加熱して熱間圧延し、Ａｒ3
変態点以上の温度で圧延を終了し、巻取り温度５００℃
以上で巻取り空冷する。巻取り温度を５００℃以上とし
たのはＢによるＮの固定を考慮してのことであり、さら
に効果的にＢによるＮを固定には６５０℃以上の温度で
の高温巻取りが好ましい。熱延コイルは酸洗後、３０％
以上の冷間圧延を施され、続いて箱型焼鈍あるいは連続
焼鈍によって再結晶温度以上Ａｃ3 変態点の間で再結晶
焼鈍され、必要に応じて過時効処理され、調質圧延され
て製品となる。再結晶焼鈍時にはＡｌによるＮの固定を
行うため、焼鈍温度を７００〜９００℃の間に設定する
ことが好ましい。過時効処理は２００〜５００℃で行
う。The cold-rolled steel sheet of the present invention containing such components is manufactured by the following method. That is, after melting the electric furnace scrap as a main iron raw material, the high N steel adjusted to the above component range, ingot, slab or continuous casting to make a steel slab, then direct hot slab, Alternatively, the hot or cold piece is reheated to 1000 to 1300 ° C. and hot-rolled, and Ar 3
Rolling is completed at a temperature above the transformation point, and the winding temperature is 500 ° C
Air is cooled by taking up the above. The reason why the winding temperature is set to 500 ° C. or higher is to consider the fixation of N by B. In order to more effectively fix N by B, high-temperature winding at a temperature of 650 ° C. or more is preferable. Hot rolled coil is 30% after pickling
Subjected to more cold rolling, subsequently recrystallized annealed between recrystallization temperature or higher Ac 3 transformation point by a box-type annealing or continuous annealing and is overaging treatment as required, and temper rolled with product Become. In order to fix N by Al at the time of recrystallization annealing, it is preferable to set the annealing temperature between 700 and 900 ° C. The overaging treatment is performed at 200 to 500C.
【００１３】[0013]
【実施例】次に本発明の実施例を説明する。表１に示す
本発明化学成分組成の鋼を電気炉で溶製して得た鋼片
を、１１００℃に再加熱し板厚２．５mmに熱延し、６８
０℃で巻取ったコイルを酸洗後、板厚を０．８mmに冷間
圧延し、７１０℃×１６時間の箱型焼鈍を行った。ほぼ
同じ工程で製造された従来鋼と併せて鋼板の機械的性質
を表２に示す。ただし、本発明鋼＃Ｄ−１鋼のみは、７
６０℃で２分保定後冷却する再結晶焼鈍と、続いて３５
０℃で５分保定する過時効処理を連続焼鈍方式で行っ
た。また、図１，２および３中●は本発明鋼の、また○
は従来鋼の強度と伸びとの関係、伸びと一様伸びとの関
係、一様伸びと塑性歪み比（ｒ値）との関係をそれぞれ
比較して示す。Next, embodiments of the present invention will be described. A steel slab obtained by melting a steel having the chemical composition of the present invention shown in Table 1 in an electric furnace was reheated to 1100 ° C. and hot rolled to a sheet thickness of 2.5 mm.
After pickling, the coil wound at 0 ° C. was cold-rolled to a thickness of 0.8 mm, and box-annealed at 710 ° C. for 16 hours. Table 2 shows the mechanical properties of the steel sheet together with the conventional steel manufactured in substantially the same process. However, only the inventive steel # D-1 steel has
Recrystallization annealing for 2 minutes at 60 ° C followed by cooling, followed by 35 minutes
An overaging treatment of holding at 0 ° C. for 5 minutes was performed by a continuous annealing method. In FIGS. 1, 2 and 3, ● represents the steel of the present invention and
Shows the relationship between the strength and elongation of conventional steel, the relationship between elongation and uniform elongation, and the relationship between uniform elongation and the plastic strain ratio (r value).
【００１４】これらの結果から本発明鋼は従来鋼と比べ
て、強度が高いにもかかわらず伸び特性、特に大きな一
様伸び特性を保持しており、その結果、塑性歪み比の優
れた高強度冷延鋼板が得られることがよく理解される。From these results, the steel of the present invention retains the elongation characteristics, particularly the large uniform elongation characteristics, in spite of its high strength, as compared with the conventional steels. As a result, the high strength steel having an excellent plastic strain ratio is obtained. It is well understood that a cold rolled steel sheet can be obtained.
【００１５】[0015]
【表１】 [Table 1]
【００１６】[0016]
【表２】 [Table 2]
【００１７】[0017]
【表３】 [Table 3]
【００１８】[0018]
【発明の効果】以上のように、本発明は、市中のスクラ
ップを再利用して冷間プレス加工性に関して中級程度以
上の、しかも高強度な冷延鋼板を提供するもので、高度
の資源有効利用技術として極めて有用である。As described above, the present invention is to provide a cold-rolled steel sheet having a middle strength or higher in cold press workability and high strength by recycling scrap from the market. It is extremely useful as an effective utilization technology.
【図面の簡単な説明】[Brief description of the drawings]
【図１】本発明鋼（●）と従来鋼（○）について強度と
伸びの関係を比較して示した図である。FIG. 1 is a diagram showing a comparison between the strength and elongation of the steel of the present invention (●) and the conventional steel (○).
【図２】本発明鋼（●）と従来鋼（○）について伸びと
一様伸びとの関係を比較して示した図である。FIG. 2 is a diagram showing a comparison between the relationship between elongation and uniform elongation for the steel of the present invention (●) and the conventional steel (○).
【図３】本発明鋼（●）と従来鋼（○）について一様伸
びと塑性歪み比との関係を比較して示した図である。FIG. 3 is a diagram showing a comparison between the relationship between the uniform elongation and the plastic strain ratio of the steel of the present invention (●) and the conventional steel (○).
───────────────────────────────────────────────────── フロントページの続き (72)発明者 池田 元 福岡県北九州市戸畑区大字中原先の浜46 −59 日本鋳鍛鋼株式会社内 (56)参考文献 特開 平３−267321（ＪＰ，Ａ) ──────────────────────────────────────────────────続 き Continuation of the front page (72) Inventor Gen Ikeda 46-59 Nakahara-san, Ohara, Tobata-ku, Kitakyushu-shi, Fukuoka Japan (56) References JP-A-3-267321 (JP, A)
Claims (5)
ることを特徴とし、電気炉で溶製した高Ｎ鋼より製造し
た冷間加工性に優れた高強度冷延鋼板。1. C: 0.005 to 0.10% by weight, Si ≦ 0.5%, Mn ≦ 1.0%, P ≦ 0.15%, S ≦ 0.035%, acid-soluble Al by weight : 0.005 to 0.10%, Ti: 0.003 to less than 0.0513% , B: 0.0001 to 0.0050%, N: 0.0055 to 0.0150% , and Ti <3.42N Characterized by being composed of Fe and unavoidable elements as a basic component, and manufactured from high N steel melted in an electric furnace.
Cold workability excellent high-strength cold-rolled steel sheet.
含み残部Ｆｅおよび不可避的元素よりなることを特徴と
し、電気炉で溶製した高Ｎ鋼より製造した冷間加工性に
優れた高強度冷延鋼板。2. C: 0.005 to 0.10% by weight, Si ≦ 0.5%, Mn ≦ 1.0%, P ≦ 0.15%, S ≦ 0.035% by weight, acid soluble Al : 0.005 to 0.10%, Ti: 0.003 to less than 0.0513% , B: 0.0001 to 0.0050%, N: 0.0055 to 0.0150% , and Ti <3.42N As a basic component, and in addition, Nb ≦ 0.1%, V ≦ 0.2%, Zr ≦ 0.15%, Cu ≦ 0.3%, Ni ≦ 0.7%, Cr ≦ 0.2 %, Mo ≦ 0.1%, Ca ≦ 0.007%, REM ≦ 0.05%, and the balance consists of Fe and inevitable elements.
A high-strength cold-rolled steel sheet with excellent cold workability manufactured from high-N steel melted in an electric furnace .
熱間圧延して５００℃以上の温度で巻取り、冷間圧延し
て冷延鋼板とし、次いでこの冷延鋼板を箱型焼鈍あるい
は連続焼鈍方式により再結晶焼鈍処理した鋼板であり、
重量で Ｃ ：０．００５〜０．１０％、 Ｓｉ≦０．５％、 Ｍｎ≦１．０％、 Ｐ ≦０．１５％、 Ｓ ≦０．０３５％、 酸可溶Ａｌ：０．００５〜０．１０％、 Ｔｉ：０．００３〜０．０５１３％未満、 Ｂ ：０．０００１〜０．００５０％、 Ｎ ：０．００５５〜０．０１５０％、かつ Ｔｉ＜３．４２Ｎ を基本成分とし、残部Ｆｅおよび不可避的元素よりなる
ことを特徴とする冷間加工性に優れた高強度冷延鋼板の
製造方法。3. A steel slab produced by melting in an electric furnace is continuously hot-rolled, wound at a temperature of 500 ° C. or more, cold-rolled into a cold-rolled steel sheet, and then the cold-rolled steel sheet is boxed. This is a steel plate that has been subjected to recrystallization annealing by die annealing or continuous annealing .
By weight C: 0.005 to 0.10%, Si ≦ 0.5%, Mn ≦ 1.0%, P ≦ 0.15%, S ≦ 0.035%, Acid-soluble Al: 0.005 to 0.10%, Ti: 0.003 to less than 0.0513% , B: 0.0001 to 0.0050%, N: 0.0055 to 0.0150% , and Ti <3.42N as a basic component, A method for producing a high-strength cold-rolled steel sheet excellent in cold workability, characterized by being composed of a balance of Fe and unavoidable elements.
間圧延して５００℃以上の温度で巻取り、冷間圧延して
冷延鋼板とし、次いでこの冷延鋼板を箱型焼鈍あるいは
連続焼鈍方式により再結晶焼鈍処理した鋼板であり、重
量で Ｃ ：０．００５〜０．１０％、 Ｓｉ≦０．５％、 Ｍｎ≦１．０％、 Ｐ ≦０．１５％、 Ｓ ≦０．０３５％、 酸可溶Ａｌ：０．００５〜０．１０％、 Ｔｉ：０．００３〜０．０５１３％未満、 Ｂ ：０．０００１〜０．００５０％、 Ｎ ：０．００５５〜０．０１５０％、かつ Ｔｉ＜３．４２Ｎ を基本成分とし、これに加えて、 Ｎｂ≦０．１％、 Ｖ ≦０．２％、 Ｚｒ≦０．１５％、 Ｃｕ≦０．３％、 Ｎｉ≦０．７％、 Ｃｒ≦０．２％、 Ｍｏ≦０．１％、 Ｃａ≦０．００７％、 ＲＥＭ≦０．０５％、のいずれか１種または２種以上を
含み残部Ｆｅおよび不可避的元素よりなることによって
製造することを特徴とする冷間加工性に優れた高強度冷
延鋼板の製造方法。4. A steel slab produced by melting in an electric furnace is continuously hot-rolled, wound at a temperature of 500 ° C. or more, cold-rolled into a cold-rolled steel sheet, and then the cold-rolled steel sheet is box-shaped. It is a steel sheet that has been subjected to recrystallization annealing treatment by annealing or continuous annealing method. C: 0.005 to 0.10%, Si ≦ 0.5%, Mn ≦ 1.0%, P ≦ 0.15%, S by weight 0.035%, acid-soluble Al: 0.005 to 0.10%, Ti: 0.003 to less than 0.0513% , B: 0.0001 to 0.0050%, N: 0.0055 to 0 0.0150% and Ti <3.42N as basic components, and in addition, Nb ≦ 0.1%, V ≦ 0.2%, Zr ≦ 0.15%, Cu ≦ 0.3%, Ni ≦ 0.7%, Cr ≦ 0.2%, Mo ≦ 0.1%, Ca ≦ 0.007%, REM ≦ 0.05% Method for producing one or a high-strength cold-rolled steel sheet excellent in cold workability, characterized in that to produce by consisting balance of Fe and incidental element comprises two or more.
あるいは４記載の冷間加工性に優れた高強度冷延鋼板の
製造方法。5. An overaging treatment after recrystallization annealing.
Alternatively, the method for producing a high-strength cold-rolled steel sheet excellent in cold workability according to 4.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2307293A JP2581887B2 (en) | 1993-02-10 | 1993-02-10 | High strength cold rolled steel sheet excellent in cold workability and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2307293A JP2581887B2 (en) | 1993-02-10 | 1993-02-10 | High strength cold rolled steel sheet excellent in cold workability and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06235047A JPH06235047A (en) | 1994-08-23 |
| JP2581887B2 true JP2581887B2 (en) | 1997-02-12 |
Family
ID=12100202
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2307293A Expired - Fee Related JP2581887B2 (en) | 1993-02-10 | 1993-02-10 | High strength cold rolled steel sheet excellent in cold workability and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2581887B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AU613063B2 (en) * | 1987-07-06 | 1991-07-25 | Komatsu Zenoah Kabushiki Kaisha | Fuel supply system |
| TW415967B (en) * | 1996-02-29 | 2000-12-21 | Kawasaki Steel Co | Steel, steel sheet having excellent workability and method of the same by electric furnace-vacuum degassing process |
| KR20020040433A (en) * | 2000-11-24 | 2002-05-30 | 이구택 | method of manufacturing a cold-rolled steel with good formability |
| CN114134367B (en) * | 2021-10-20 | 2023-02-21 | 中国科学院金属研究所 | High-strength hydrogen embrittlement-resistant membrane with MP-5 mark and preparation method thereof |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6199631A (en) * | 1984-10-22 | 1986-05-17 | Kawasaki Steel Corp | Manufacture of thin steel sheet for deep drawing |
| JPH0759735B2 (en) * | 1988-07-20 | 1995-06-28 | 川崎製鉄株式会社 | Steel sheet for direct enamel with excellent bubble resistance and black spot defects |
| JPH03267321A (en) * | 1990-03-16 | 1991-11-28 | Nippon Steel Corp | Production of cold rolled steel sheet for deep drawing |
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1993
- 1993-02-10 JP JP2307293A patent/JP2581887B2/en not_active Expired - Fee Related
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| Publication number | Publication date |
|---|---|
| JPH06235047A (en) | 1994-08-23 |
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