JP2599466B2 - Low yield ratio structural steel excellent in non-aging property and method of manufacturing the same - Google Patents
Low yield ratio structural steel excellent in non-aging property and method of manufacturing the sameInfo
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- JP2599466B2 JP2599466B2 JP1268090A JP26809089A JP2599466B2 JP 2599466 B2 JP2599466 B2 JP 2599466B2 JP 1268090 A JP1268090 A JP 1268090A JP 26809089 A JP26809089 A JP 26809089A JP 2599466 B2 JP2599466 B2 JP 2599466B2
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は非時効性に優れた低降伏比構造用鋼材および
その製造方法に関するものである。Description: TECHNICAL FIELD The present invention relates to a low yield ratio structural steel excellent in non-aging and a method for producing the same.
（従来の技術） 近年、建築用構造物に使用される鋼材（鋼板、鋼管あ
るいは形鋼ほか）をはじめとする構造用鋼材において、
耐震性に優れた低降伏比鋼が要求されており、種々の低
降伏比鋼材ならびにその製造方法の提案がなされてい
る。(Prior art) In recent years, in structural steel materials such as steel materials (steel plates, steel pipes or shaped steels) used for building structures,
There is a demand for low-yield-ratio steels having excellent seismic resistance, and various low-yield-ratio steel materials and methods for producing the same have been proposed.
その解決の手段は、軟質相と硬質相の組合せ、すなわ
ち２相鋼化によるものが殆どであり、たとえば、フェラ
イト−マルテンサイト（あるいはベイナイト）２相鋼化
による低降伏比化の例として、特公平１−16888号、特
公昭58−10442号公報が上げられる。Most of the solutions are based on a combination of a soft phase and a hard phase, that is, a dual-phase steel. For example, as an example of a low yield ratio by a ferritic-martensitic (or bainite) dual-phase steel, there is a special method. Japanese Patent Publication No. Hei 1-16888 and Japanese Patent Publication No. 58-10442 are published.
しかしながら、これらの鋼材は圧延まま（製造まま）
では良好な低降伏比を有するが、曲げ加工あるいは造管
加工等の冷間加工を受けると歪時効により降伏比が著し
く増大し、所期の特性（低降伏比）を満足し得なくなる
という問題点があった。However, these steels are as-rolled (as-produced)
Has a low yield ratio, but when subjected to cold working such as bending or pipe forming, the yield ratio increases significantly due to strain aging, and the desired characteristics (low yield ratio) cannot be satisfied. There was a point.
（発明が解決しようとする課題） 本発明の目的は、冷間加工によっても時効を起こさな
い、すなわち冷間加工後も良好な低降伏比を確保でき
る、非時効性に優れた高強度低降伏比構造用鋼材ならび
にその製造方法を提供するものである。(Problems to be Solved by the Invention) An object of the present invention is to provide a high-strength low-yield excellent in non-aging property which does not cause aging even by cold working, that is, can secure a good low yield ratio even after cold working. An object of the present invention is to provide a specific structural steel material and a method for producing the same.
（課題を解決するための手段） 本発明の要旨とするところは重量％で、C:0.02〜0.05
％、Si:2.5％以下、Mn:2.0％以下、P:0.03％以下、S:0.
01％以下、Al:0.10％以下、N:0.001〜0.010％、でかつT
iを（Ti−3.4N）/C＝４〜６、とし、必要に応じてこれ
にNi:1.0％以下、Cu:1.0％以下、Cr:1.0％以下、Mo:1.0
％以下、Ca:0.0005〜0.005％のうちいずれか１種、また
は２種以上をさらに含有し、残部がFeおよび不可避的不
純物からなり、C,Nを固定して非時効性化し、それによ
って冷間加工後の降伏比の上昇を防止したことを特徴と
する非時効性に優れた低降伏比構造用鋼材である。(Means for Solving the Problems) The gist of the present invention is as follows: C: 0.02 to 0.05
%, Si: 2.5% or less, Mn: 2.0% or less, P: 0.03% or less, S: 0.
01% or less, Al: 0.10% or less, N: 0.001 to 0.010%, and T
i is (Ti−3.4N) / C = 4 to 6, and if necessary, Ni: 1.0% or less, Cu: 1.0% or less, Cr: 1.0% or less, Mo: 1.0%
% Or less, Ca: 0.0005 to 0.005%, which further contains one or more of the following, and the balance consists of Fe and unavoidable impurities. This is a low yield ratio structural steel excellent in non-aging characteristics, in which an increase in yield ratio after cold working is prevented.
更に本発明は重量％で、C:0.02〜0.05％、Si:2.5％以
下、Mn:2.0％以下、P:0.03％以下、S:0.01％以下、Al:
0.10％以下、N :0.001〜0.010％でかつTiを（Ti−3.4
N）/C＝４〜６とし、必要に応じてこれにNi:1.0％以
下、Cu:1.0％以下、Cr:1.0％以下、Mo:1.0％以下、Ca:
0.0005〜0.005％のうちいずれか１種、または２種以上
をさらに含有し、残部がFeおよび不可避的不純物からな
る鋼片を900℃以上の温度に加熱後、700℃以上の温度で
圧延を終了し、以後空冷ないしは加速冷却し、C,Nを固
定して非時効性化し、それによって冷間加工後の降伏比
の上昇を防止することを特徴とする非時効性に優れた低
降伏比構造用鋼材の製造方法である。Further, in the present invention, C: 0.02 to 0.05%, Si: 2.5% or less, Mn: 2.0% or less, P: 0.03% or less, S: 0.01% or less, Al:
0.10% or less, N: 0.001 to 0.010% and Ti (Ti-3.4
N) / C = 4 to 6, and if necessary, Ni: 1.0% or less, Cu: 1.0% or less, Cr: 1.0% or less, Mo: 1.0% or less, Ca:
After heating a steel slab containing at least one of 0.0005 to 0.005% and the remainder consisting of Fe and unavoidable impurities to a temperature of 900 ° C or higher, rolling is completed at a temperature of 700 ° C or higher. Low-yield-ratio structure with excellent non-aging properties, characterized by air-cooling or accelerated cooling, fixing C and N to de-aging, thereby preventing the yield ratio from increasing after cold working. It is a manufacturing method of steel materials for use.
本発明の低降伏比構造用鋼材は冷間加工後も良好な低
降伏比を有することを特徴とする非時効性に優れた高強
度低降伏比構造用鋼材である。従来の低降伏比鋼材で
は、圧延ままでは良好な低降伏比を示すものの、ひとた
び冷間加工を加えると歪時効効果により降伏点が著しく
上昇し、冷間加工ままでは初期の低降伏比を達成し得な
いという問題点があった。The low-yield-ratio structural steel material of the present invention is a high-strength low-yield-ratio structural steel excellent in non-aging properties, having a good low yield ratio even after cold working. Conventional low-yield-ratio steels show good low-yield ratios as-rolled, but once cold-worked, the yield point rises significantly due to the strain aging effect, achieving the initial low-yield ratio when cold-worked There was a problem that it could not be done.
この問題点を解決するため、非時効性に優れ、かつ低
降伏比を満足するとともに所要の強度レベルを確保する
という観点からフェライト単相鋼の有する特性を最大限
に活用することを試みた。In order to solve this problem, an attempt was made to make the most of the properties of the ferritic single-phase steel from the viewpoint of excellent non-aging properties, satisfying a low yield ratio, and securing a required strength level.
以下、本発明鋼材における化学成分の限定理由につい
て説明する。Hereinafter, the reasons for limiting the chemical components in the steel material of the present invention will be described.
まず、非時効性に関しては、時効を生じる原因となる
侵入型固溶原子であるＣならびにＮの固定化が必須であ
る。本発明においてはTiによるC,Nの固定化を試みた。
すなわち、TiをC,Nの当量以上添加することによりC,Nの
固定化を計った（（Ti−3.4N）/C≧４）。First, as for non-aging properties, it is essential to fix C and N, which are interstitial solid solution atoms that cause aging. In the present invention, an attempt was made to fix C and N with Ti.
That is, C and N were immobilized by adding Ti or more in equivalent amounts of C and N ((Ti−3.4N) / C ≧ 4).
一方、Tiを過量に添加するとTiCの粗大化が起こり、T
iCによる析出強化が利用できなくなるため、高強度化が
困難となる。そこで、TiとC,Nの適正なバランス域を（T
i−3.4N）/C＝４〜６とした。On the other hand, if Ti is added in an excessive amount, coarsening of TiC occurs, and T
Since precipitation strengthening by iC cannot be used, it is difficult to increase the strength. Therefore, an appropriate balance between Ti and C, N
i-3.4N) / C = 4-6.
Ｃ量は非時効性という観点からは少ない方が好まし
い。しかしながら、溶接性の観点から、その下限を0.02
％とした。また、Ｃ量が多くなるとＣを固定するための
Tiの添加量が増大し、溶接性を阻害する。そのためＣ量
の上限を0.05％とした。It is preferable that the C content is small from the viewpoint of non-aging property. However, from the viewpoint of weldability, the lower limit is 0.02
%. Also, when the amount of C increases, the amount of C
The addition amount of Ti increases and hinders weldability. Therefore, the upper limit of the C content is set to 0.05%.
Siは脱酸上鋼に含まれる元素である。また、固溶強化
によるフェライトマトリックス強化の点で有用である。
一般の炭素鋼ではSiの過剰添加は溶接性、HAZ靱性を阻
害するが、本発明鋼ではＣをTiで固定しているため、そ
の添加量は2.5％まで可能である。Si is an element contained in the deoxidized upper steel. Further, it is useful in strengthening the ferrite matrix by solid solution strengthening.
In general carbon steel, excessive addition of Si impairs weldability and HAZ toughness, but in the steel of the present invention, since C is fixed with Ti, the addition amount can be up to 2.5%.
Mnは脱酸上鋼に含まれる元素である。また、強度、靱
性を確保する上で有用である。しかしMn量が多すぎると
溶接性、HAZ靱性の劣化を招くためその上限を20％とし
た。Mn is an element contained in the deoxidized upper steel. Further, it is useful for securing strength and toughness. However, if the amount of Mn is too large, the weldability and the HAZ toughness are deteriorated, so the upper limit is set to 20%.
P,Sは不可避的不純物として鋼中に含まれる。これら
は母材ならびに溶接部の靱性を劣化させるため、その量
は極力少ない方が好ましく、本発明鋼ではP,Sの上限量
をそれぞれ0.03％,0,01％以下とした。P and S are contained in steel as inevitable impurities. Since these deteriorate the toughness of the base metal and the welded portion, the amounts thereof are preferably as small as possible. In the steel of the present invention, the upper limits of P and S are set to 0.03% and 0.01% respectively.
Alは一般に脱酸上鋼に含まれる元素であるが、Siおよ
びMnあるいはTiによっても脱酸は行なわれるので、本発
明ではAlについては下限を限定しない。しかし、Al量が
多くなると鋼の清浄度が悪くなり、HAZ靱性が劣化する
ので上限を0.1％とした。Al is generally an element contained in the deoxidized upper steel, but the deoxidation is also performed by Si, Mn or Ti, and therefore, the present invention does not limit the lower limit of Al. However, when the amount of Al increases, the cleanliness of the steel deteriorates and the HAZ toughness deteriorates. Therefore, the upper limit was set to 0.1%.
Ｎは一般に不可避的不純物として鋼中に含まれるが、
非時効性の観点からはＮ量は少ないことが好ましい。し
かしながら、本発明鋼ではTiをＮに対して当量以上添加
しており、Ｎの固定化はTiによって十分に行える。従っ
て、TiNによるHAZ靱性向上のための必要最小量として、
Ｎ量の下限を0.001％とした。また、Ｎの過量添加はHAZ
靱性の劣化を招くため、その上限を0.01％とした。N is generally contained in steel as an unavoidable impurity,
From the viewpoint of non-aging property, the N content is preferably small. However, in the steel of the present invention, Ti is added in an amount equivalent to N or more, and N can be sufficiently fixed by Ti. Therefore, as the minimum necessary amount for improving the HAZ toughness by TiN,
The lower limit of the amount of N was set to 0.001%. The excessive addition of N is HAZ
Since the toughness deteriorates, the upper limit is made 0.01%.
本発明鋼においては、さらに必要によりNi:0.05〜0.5
％、Cu:0.05〜0.5％、Cr:1.0％以下、Mo:1.0％以下、C
a:0.0005〜0.005％のうちいずれか１種、または２種以
上を含有させる。In the steel of the present invention, if necessary, Ni: 0.05 to 0.5
%, Cu: 0.05-0.5%, Cr: 1.0% or less, Mo: 1.0% or less, C
a: 0.0005 to 0.005% of any one or two or more of them are contained.
これらの元素を含有させる主たる目的は本発明鋼の特
徴を損なうことなく、強度、靱性の向上および製造板厚
の拡大を可能にするところにあり、その添加量は溶接性
およびHAZ靱性等の面から自ずと制限されるべき性質の
ものである。The main purpose of including these elements is to improve strength and toughness and to increase the thickness of the manufactured plate without impairing the characteristics of the steel of the present invention. Is of a nature that should be naturally restricted.
NiはHAZの硬化性および靱性に悪影響を与えることな
く母材の強度、靱性を向上させる特性をもつが、1.0％
を超えるとHAZの硬化性および靱性上好ましくないた
め、上限を1.0％とした。Ni has the property of improving the strength and toughness of the base material without adversely affecting the hardening and toughness of HAZ, but 1.0%
If it exceeds, the curability and toughness of HAZ are unfavorable, so the upper limit was made 1.0%.
CuはNiとほぼ同様の効果を持つとともに、耐食性、耐
水素誘起割れ特性にも効果がある。しかし、1.0％を超
えると圧延中にCu−クラックが発生し製造が困難にな
る。このため、上限を1.0％とした。Cu has almost the same effect as Ni, and also has an effect on corrosion resistance and hydrogen-induced cracking resistance. However, if it exceeds 1.0%, Cu-cracks are generated during rolling, and the production becomes difficult. Therefore, the upper limit is set to 1.0%.
Crは母材の強度を高める元素であるが、Cr量が１％を
超えると溶接性やHAZ靱性を劣化させるため、上限を1.0
％とした。Cr is an element that increases the strength of the base material. However, if the Cr content exceeds 1%, the weldability and HAZ toughness are deteriorated.
%.
Moは母材の強度、靱性を共に向上させる元素である
が、1.0％を超えると溶接部靱性および溶接性の劣化を
招き好ましくないため、上限を1/0％とした。Mo is an element that improves both the strength and toughness of the base material. However, if it exceeds 1.0%, the toughness and weldability of the welded part are undesirably deteriorated. Therefore, the upper limit is set to 1/0%.
Caは硫化物の形態を制御し、シャルピー吸収エネルギ
ーを増加させ低温靱性を向上させるほか、耐水素誘起割
れ性の改善にも効果を発揮する。しかし、Ca量は0.0005
％未満では実用上効果がなく、また、0.005％を超える
とCaS,CaOが多量に生成して大型介在物となり、鋼の靱
性のみならず清浄度も害し、さらに溶接性にも悪影響を
与えるので、Ca添加量の範囲を0.0005〜0.005％とし
た。Ca controls the sulfide morphology, increases Charpy absorbed energy, improves low-temperature toughness, and has an effect on improving hydrogen-induced cracking resistance. However, the amount of Ca is 0.0005
If it is less than 0.005%, there is no practical effect, and if it exceeds 0.005%, CaS and CaO are generated in large amounts and become large inclusions, which impair not only the toughness but also the cleanliness of the steel, and also have an adverse effect on the weldability. And the amount of Ca added was set to 0.0005 to 0.005%.
以上の成分系を有する本発明鋼は、非時効性に優れ、
かつ低降伏比を満足するとともに所要の強度レベルを確
保し得る画期的な低降伏比構造用鋼材である。The steel of the present invention having the above component system has excellent non-aging properties,
It is an epoch-making low yield ratio structural steel material that satisfies a low yield ratio and can secure a required strength level.
次に、以上のような成分系を有する鋼材の製造法につ
いて述べる。Next, a method for producing a steel material having the above-described component system will be described.
まず、鋼片の加熱温度は900℃以上とする必要があ
る。加熱温度が、900℃未満になると、圧延終了が低く
なりすぎるため、所要の材質が得られなくなる。そこで
加熱温度の下限を900℃とする必要がある。First, the heating temperature of the billet needs to be 900 ° C. or higher. If the heating temperature is lower than 900 ° C., the end of rolling becomes too low, and the required material cannot be obtained. Therefore, it is necessary to set the lower limit of the heating temperature to 900 ° C.
加熱温度の上限については特に制約されるものではな
いで、母材靱性という観点からは1250℃以下程度とする
ことが好ましい。なお、鋼片鋳造後Ar3温度以下に冷却
後再加熱することなく、すなわち鋼片鋳造後直ちにある
いは鋼片鋳造後Ar3温度以上での保熱過程を経た後直ち
に圧延を行なってもよい。The upper limit of the heating temperature is not particularly limited, and is preferably about 1250 ° C. or less from the viewpoint of base metal toughness. Incidentally, without re-heating after cooling below Ar 3 temperature after the steel strip casting, i.e. immediately may perform rolling after a heat retaining process at immediately after the steel strip casting or billet after casting Ar 3 temperature or above.
圧延終了温度を700℃以上とする理由は、この温度よ
り低い温度で圧延を行なうとフェライトの加工が過度に
行なわれ、母材靱性が劣化するためである。また、圧延
終了温度の上限は特に制約されるものではないが、靱性
確保の観点からは1000℃以下とすることが好ましい。な
お圧延後の鋼材の冷却は空冷あるいは加速冷却のいずれ
のプロセスを適用してもよい。The reason for setting the rolling end temperature to 700 ° C. or higher is that if rolling is performed at a temperature lower than this temperature, ferrite is excessively worked and base material toughness is deteriorated. The upper limit of the rolling end temperature is not particularly limited, but is preferably 1000 ° C. or lower from the viewpoint of securing toughness. The cooling of the steel material after rolling may be performed by any of air cooling and accelerated cooling.
なお、本発明は種々の鋼材に適用が可能であるが、主
として引張強度50〜80kgf/mm2、板厚100mm以下の厚鋼板
並びに熱延鋼板に適用されることが好ましい。The present invention can be applied to various steel materials, but is preferably applied mainly to a thick steel plate having a tensile strength of 50 to 80 kgf / mm 2 and a plate thickness of 100 mm or less and a hot-rolled steel plate.
（実施例） 第１表に供試鋼の化学成分を、第２表に各鋼の製造条
件と、圧延まま並びに冷間加工後の各鋼の機械的性質を
示す。(Example) Table 1 shows the chemical composition of the test steel, and Table 2 shows the manufacturing conditions of each steel, and the mechanical properties of each steel as it is rolled and after cold working.
第1,第２表において、鋼Ａ〜Ｉは本発明鋼、Ｊ〜Ｋは
比較鋼を示す。In Tables 1 and 2, steels A to I indicate inventive steels and J to K indicate comparative steels.
本発明鋼Ａ〜Ｉは高強度を有するとともに、圧延まま
のみならず10％の冷間加工後においても80％以下の極め
て良好な低降伏比を有する。The steels A to I of the present invention have high strength and a very good low yield ratio of not more than 80% not only as-rolled but also after cold working of 10%.
これに対して、比較鋼Ｊは圧延ままでは良好な低降伏
比を示すものの、Ti量の不足により（eTi＝3.8）、C,N
の固定が不十分であり、冷間加工後の降伏比が97％と極
めて高くなっている。また、比較鋼ＫはeTi＝7.1とTi量
が過剰なため、TiCの粗大化が生じ強度が著しく低い。
比較鋼ＬはTi量が低く、TiCによる析出強化効果がない
ため強度が低い。また、C,Nの固定が不十分なため、冷
間加工後の降伏比が96％と極めて高くなっている。On the other hand, although the comparative steel J shows a good low yield ratio as it is rolled, C, N
The yield ratio after cold working is extremely high at 97%. Further, the comparative steel K has eTi = 7.1 and an excessive amount of Ti, so that TiC is coarsened and the strength is extremely low.
The comparative steel L has a low Ti content and does not have a precipitation strengthening effect by TiC, and thus has a low strength. Further, since the fixation of C and N is insufficient, the yield ratio after cold working is extremely high at 96%.
（発明の効果） 本発明鋼の降伏比は冷間加工後においても極めて低く
（非時効性に優れ）、従来鋼にはない優れた低降伏比特
性を有する。 (Effect of the Invention) The yield ratio of the steel of the present invention is extremely low even after cold working (excellent in non-aging properties), and has excellent low yield ratio characteristics not available in conventional steels.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 為広 博 千葉県君津市君津１ 新日本製鐵株式会 社君津製鐵所内 (56)参考文献 特開 昭63−206451（ＪＰ，Ａ) 特開 昭56−142852（ＪＰ，Ａ) ────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Hiroshi Tamehiro 1 Kimitsu, Kimitsu City, Chiba Prefecture Nippon Steel Corporation Kimitsu Works (56) References JP-A-63-206451 (JP, A) JP-A-63-206451 56-142852 (JP, A)
Claims (4)
て非時効性化し、 それによって冷間加工後の降伏比の上昇を防止したこと
を特徴とする非時効性に優れた低降伏比構造用鋼材。[Claim 1] In terms of% by weight, C: 0.02 to 0.05%, Si: 2.5% or less, Mn: 2.0% or less, P: 0.03% or less, S: 0.01% or less, Al: 0.10% or less, N: 0.001 to 0.010%, Ti is (Ti-3.4N) / C = 4-6, balance is Fe and unavoidable impurities, C and N are fixed to make it non-aging, and thereby yield ratio after cold working A low yield ratio structural steel with excellent non-aging properties, characterized in that it is prevented from rising.
特徴とする請求項１記載の非時効性に優れた低降伏比構
造用鋼材。2. In weight%, Ni: 1.0% or less, Cu: 1.0% or less, Cr: 1.0% or less, Mo: 1.0% or less, Ca: 0.0005 to 0.005%, any one or two of the following: The low yield ratio structural steel material excellent in non-aging property according to claim 1, characterized by containing the above.
上の温度に加熱後、700℃以上の温度で圧延を終了し、
以後空冷ないしは加速冷却し、C,Nを固定して非時効性
化し、それによって冷間加工後の降伏比の上昇を防止す
ることを特徴とする非時効性に優れた低降伏比構造用鋼
材の製造方法。3. In% by weight, C: 0.02-0.05%, Si: 2.5% or less, Mn: 2.0% or less, P: 0.03% or less, S: 0.01% or less, Al: 0.10% or less, N: 0.001 or less 0.010%, Ti (Ti-3.4N) / C = 4 ~ 6, the rest is heated to 900 ℃ or more steel slab consisting of Fe and unavoidable impurities, then rolling is finished at 700 ℃ or more,
After that, it is air-cooled or accelerated cooled, C and N are fixed to make it non-aging, and thereby the yield ratio after cold working is prevented from increasing, so that it has excellent non-aging property and low yield ratio structural steel Manufacturing method.
鋼片であることを特徴とする請求項３記載の非時効性に
優れた低降伏比構造用鋼材の製造方法。4. In% by weight, one or two of Ni: 1.0% or less, Cu: 1.0% or less, Cr: 1.0% or less, Mo: 1.0% or less, Ca: 0.0005 to 0.005% The method for producing a low yield ratio structural steel excellent in non-aging according to claim 3, wherein the steel is a slab further containing the above.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1268090A JP2599466B2 (en) | 1989-10-17 | 1989-10-17 | Low yield ratio structural steel excellent in non-aging property and method of manufacturing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1268090A JP2599466B2 (en) | 1989-10-17 | 1989-10-17 | Low yield ratio structural steel excellent in non-aging property and method of manufacturing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03130345A JPH03130345A (en) | 1991-06-04 |
| JP2599466B2 true JP2599466B2 (en) | 1997-04-09 |
Family
ID=17453752
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1268090A Expired - Fee Related JP2599466B2 (en) | 1989-10-17 | 1989-10-17 | Low yield ratio structural steel excellent in non-aging property and method of manufacturing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2599466B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103998638B (en) * | 2011-12-12 | 2016-05-18 | 杰富意钢铁株式会社 | The steel plate that ageing resistance is good and manufacture method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5942742B2 (en) * | 1980-04-09 | 1984-10-17 | 新日本製鐵株式会社 | High strength cold rolled steel plate for deep drawing with low yield ratio |
| JPH07103444B2 (en) * | 1987-02-23 | 1995-11-08 | 日新製鋼株式会社 | Soft cold-rolled steel sheet with excellent weldability |
-
1989
- 1989-10-17 JP JP1268090A patent/JP2599466B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH03130345A (en) | 1991-06-04 |
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