JPH0617125A - Production of hot rolled steel plate for line pipe - Google Patents
Production of hot rolled steel plate for line pipeInfo
- Publication number
- JPH0617125A JPH0617125A JP19928892A JP19928892A JPH0617125A JP H0617125 A JPH0617125 A JP H0617125A JP 19928892 A JP19928892 A JP 19928892A JP 19928892 A JP19928892 A JP 19928892A JP H0617125 A JPH0617125 A JP H0617125A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- toughness
- steel plate
- hot
- line pipe
- 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.)
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、ラインパイプに使用す
る熱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 manufacturing a hot rolled steel sheet used for a line pipe.
【０００２】[0002]
【従来の技術】ラインパイプに用いられるスパイラル鋼
管や電縫鋼管の素材である熱延鋼板については、これま
でＴｉ−Ｎｂ系、Ｎｂ−Ｖ系を主体とした析出強化型の
高強度高靱性鋼が使用されてきた。しかし、最近になっ
て、ラインパイプの破壊に対する余裕度の確保等の点か
ら、ＹＲ（降伏比）の上限が厳しく規制されるケースが
増加している。2. Description of the Related Art Hot-rolled steel sheets, which are raw materials for spiral steel pipes and electric resistance welded steel pipes used for line pipes, have hitherto been found to be precipitation-strengthened high-strength and high-toughness steels mainly composed of Ti-Nb and Nb-V. Has been used. However, recently, there are increasing cases where the upper limit of the YR (yield ratio) is strictly regulated in order to secure a margin against breakage of the line pipe.
【０００３】一般に、低ＹＲ化にはＣ量の増加が有効と
されているが、電縫鋼管のシーム熱処理後のＨＡＺ靱性
劣化、周溶接部のＨＡＺ靱性劣化等の観点から、ライン
パイプ用途でＣの増加による低ＹＲ化を図ることは困難
である。また近年、母材に要求される厳しい低温靱性を
確保する上からも好ましくないのが実情である。Generally, increasing the amount of C is effective for lowering the YR, but from the viewpoint of deterioration of HAZ toughness after seam heat treatment of ERW steel pipe, deterioration of HAZ toughness of peripheral welds, etc., it is used for line pipe applications. It is difficult to reduce YR by increasing C. Further, in recent years, it is a fact that it is not preferable from the viewpoint of securing the severe low temperature toughness required for the base material.
【０００４】このような状況を踏まえて、所謂制御圧延
により低ＹＲ化を図る技術の開発が各方面で進められて
おり、例えば、特開昭５５−９１９３４号公報には、熱
間圧延を（Ａｒ3 点±５０℃）の仕上温度で行ない、圧
延終了から６５０℃までの前段を１〜５０℃／秒の比較
的小さな冷却速度で冷却してオーステナイトを生成し、
６５０℃から巻き取りまでの後段を１０〜１００℃／秒
の比較的大きな冷却速度で冷却してオーステナイトをマ
ルテンサイト変態させる低ＹＲ鋼板の製造方法が開示さ
れている。In view of such circumstances, development of a technique for lowering YR by so-called controlled rolling is being advanced in various fields. For example, Japanese Patent Laid-Open No. 55-91934 discloses hot rolling ( Ar 3 points ± 50 ° C) at a finishing temperature, and cooling the front stage from the end of rolling to 650 ° C at a relatively low cooling rate of 1 to 50 ° C / sec to generate austenite,
Disclosed is a method for producing a low YR steel sheet in which austenite is transformed into martensite by cooling the subsequent stage from 650 ° C to winding at a relatively large cooling rate of 10 to 100 ° C / sec.
【０００５】また、特開昭６４−４７８１５号公報に
は、Ａｒ3 点以上の温度で熱間圧延を行ない、Ａｒ3 点
から（Ａｒ3 点−８０℃）までを１０℃／分程度の速度
で冷却してフェライトを析出させ、これに続き加速冷却
（８℃／分以上）で残留オーステナイトをマルテンサイ
トまたはベイナイト、或いはそれらの混合組織に変態さ
せる低ＹＲ厚鋼板の製造方法が開示されている。Further, in JP-A-64-47815, hot rolling is carried out at a temperature of Ar 3 point or higher, and a speed of about 10 ° C./minute from Ar 3 point to (Ar 3 point-80 ° C.). There is disclosed a method for producing a low YR thick steel plate, in which ferrite is precipitated by cooling at a low temperature, followed by accelerated cooling (8 ° C./min or more) to transform retained austenite into martensite, bainite, or a mixed structure thereof. .
【０００６】[0006]
【発明が解決しようとする課題】前者の製法（特開昭５
５−９１９３４号）では、一部オーステナイトを残留さ
せたフェライト＋マルテンサイトの複相鋼板が得られ、
後者の製法（特開昭６４−４７８１５号）では、フェラ
イト＋（マルテンサイトおよび／またはベイナイト）の
複相鋼板が得られるとしている。これらの鋼板は、その
複相組織ゆえに、高強度でＹＲが低い。[Problems to be Solved by the Invention] The former manufacturing method (Japanese Patent Laid-Open No. Sho 5)
No. 5-91934), a ferrite + martensite multi-phase steel sheet in which austenite is partially retained is obtained,
The latter manufacturing method (JP-A-64-47815) states that a ferrite + (martensite and / or bainite) multi-phase steel sheet can be obtained. These steel sheets have high strength and low YR because of their multiphase structure.
【０００７】しかし、前者は自動車用薄板を主たる対象
としており、マルテンサイト組織および残留オーステナ
イトを有しているが故にラインパイプ用鋼材に要求され
る母材低温靱性ならびに溶接ＨＡＺ靱性の観点からライ
ンパイプ用鋼材としては不適である。[0007] However, the former is mainly intended for automobile thin plates, and has a martensite structure and retained austenite, and therefore has a low temperature base metal toughness and a welded HAZ toughness required for steel products for line pipes. Not suitable as a steel material for use.
【０００８】後者は土木建築用鋼材である厚板鋼板を主
に対象としており、実施例に見られるＣ量（0.１０〜0.
１６％）およびＳｉ量（0.２５％〜0.３８％）の値は高
く、溶接部靱性を考慮すべきラインパイプ用鋼材として
の充分な性能は確保できない。また、巻取温度について
の配慮もなされていない。The latter is mainly intended for thick steel plates which are steel materials for civil engineering and construction, and the C content (0.10 to 0.
16%) and the amount of Si (0.25% to 0.38%) are high, and sufficient performance cannot be secured as a steel material for a line pipe in which the toughness of the welded portion should be taken into consideration. Moreover, no consideration is given to the winding temperature.
【０００９】本発明の目的は、低ＹＲで、しかもライン
パイプ用鋼材として充分な強度、靱性および溶接性を保
有する熱延鋼板の製造方法を提供することにある。An object of the present invention is to provide a method for producing a hot-rolled steel sheet having low YR and having sufficient strength, toughness and weldability as a steel material for line pipes.
【００１０】[0010]
【課題を解決するための手段】ラインパイプ用鋼材とし
ての強度および靱性を損なわずにＹＲを低下させる手段
として、本発明者らは変態強化機能をもつＭｏ添加鋼に
着目した。母材強度および靱性に及ぼす各種合金元素の
影響を図１に示し、各種合金鋼を電縫鋼管としたときの
シーム熱処理部靱性を図２に示す。基本成分はいずれも
0.０６Ｃ−0.１５Ｓｉ−1.２０Ｍｎ−0.０４５Ｎｂ−0.
０１５Ｔｉである。As a means for reducing YR without impairing the strength and toughness as a steel material for line pipes, the present inventors have focused on Mo-added steel having a transformation strengthening function. The effect of various alloying elements on the strength and toughness of the base metal is shown in FIG. 1, and the toughness of the seam heat treated part when various alloyed steels are used as electric resistance welded steel pipes is shown in FIG. All basic ingredients
0.06C-0.15Si-1.20Mn-0.045Nb-0.
015Ti.
【００１１】Ｍｏ添加による変態強化型鋼は、Ｎｂ添加
による析出強化型鋼に比して靱性確保が容易であり、Ｍ
ｎ添加による変態強化型鋼に比しては、強度確保が容易
である。また、Ｍｏ添加鋼から製造した電縫鋼管は、シ
ーム熱処理温度の許容範囲が広く、安定して高靱性が得
られることもラインパイプ用鋼材としては有利である。The transformation-strengthened steel with addition of Mo is easier to secure toughness than the precipitation-strengthened steel with addition of Nb.
It is easier to secure the strength as compared with the transformation strengthened steel by the addition of n. Further, the electric resistance welded steel pipe manufactured from the Mo-added steel has a wide allowable range of the seam heat treatment temperature and can stably obtain high toughness, which is also advantageous as a steel material for a line pipe.
【００１２】そこで、本発明者は、このＭｏ添加鋼にラ
インパイプ用鋼材に必要な強度および靱性を与え、且
つ、最近の低ＹＲに対する要求を満足させるべく、組成
および製造条件について検討を行った。その結果、オー
ステナイトのマルテンサイト変態を抑え、鋼板組織をフ
ェライト＋微細ベイナイトの２相組織とするのが靱性を
確保するのに有効なこと、その２相化のためには、熱間
圧延の仕上温度、圧延後の冷却速度および巻取温度の厳
密なコントロールが必要なことを知見した。[0012] Therefore, the present inventor studied the composition and manufacturing conditions in order to provide the Mo-added steel with the strength and toughness required for steel for line pipes and to satisfy the recent requirements for low YR. . As a result, suppressing the martensitic transformation of austenite and making the steel sheet structure a two-phase structure of ferrite + fine bainite is effective for securing toughness. It was found that strict control of temperature, cooling rate after rolling and coiling temperature was required.
【００１３】本発明は上記知見に基づきなされたもの
で、重量比でＣ：0.０４％以上0.１０％未満、Ｓｉ：0.
０３〜0.１５％、Ｍｎ：1.０〜1.６％、Ｍｏ：0.２０〜
0.３０％、Ｎｂ：0.０１０〜0.０５％、Ｔｉ：0.０１〜
0.０３０％を含み、残部Ｆｅおよび不可避不純物からな
る鋼を、加熱後、（Ａｒ3 点＋２０℃）以上の仕上温度
で熱間圧延し、更に、（Ａｒ3 点−８０℃）までの間を
１０℃／秒以下の冷却速度で緩冷却して、５００℃以下
の温度で巻き取ることを特徴とするラインパイプ用熱延
鋼板の製造方法を要旨とする。The present invention has been made based on the above-mentioned findings. The weight ratio of C: 0.04% or more and less than 0.10%, Si: 0.
03-0.15%, Mn: 1.0-1.6%, Mo: 0.20-
0.30%, Nb: 0.000-0.05%, Ti: 0.01-
Steel containing 0.030% and the balance Fe and unavoidable impurities is heated and then hot-rolled at a finishing temperature of (Ar 3 point + 20 ° C) or higher, and further until (Ar 3 point-80 ° C). A method for producing a hot-rolled steel sheet for a line pipe is characterized in that is slowly cooled at a cooling rate of 10 ° C./second or less and is wound at a temperature of 500 ° C. or less.
【００１４】なお、特開昭５５−９１９３４号公報に開
示された鋼板製造法は、素材鋼中にＭｏを含まず、圧延
仕上温度も（Ａｒ3 点±５０℃）と低く、巻取温度につ
いては何も考慮されていない。従って、鋼板組織はフェ
ライト＋マルテンサイトの２相組織となり、ベイナイト
は生成されない。マルテンサイトが含まれると、ライン
パイプ用鋼材に要求される靱性を確保するのが困難にな
る。また、圧延仕上温度の低さに起因して、加工フェラ
イトの生成によるＹＲの上昇、加工オーステナイトの生
成による強度の異方性、初期フェライト生成の不安定も
生じる。更に、強度確保のためＳｉが多く添加されてい
るので周溶接性もラインパイプ用鋼材としては充分とは
言えない。The steel sheet manufacturing method disclosed in JP-A-55-91934 does not contain Mo in the material steel and has a low rolling finishing temperature (Ar 3 points ± 50 ° C.). Nothing is considered. Therefore, the steel sheet structure has a two-phase structure of ferrite + martensite, and bainite is not formed. The inclusion of martensite makes it difficult to ensure the toughness required for steel products for line pipes. Further, due to the low rolling finish temperature, YR rises due to the formation of work ferrite, anisotropy of strength due to the formation of work austenite, and instability of initial ferrite formation occur. Further, since a large amount of Si is added to secure the strength, the circumferential weldability is not sufficient as a steel material for line pipes.
【００１５】特開昭６４−４７８１５号公報に開示され
た鋼板製造法については、条件によってはフェライト＋
ベイナイトの２相組織が得られるとしているが、実施例
を見る限り、Ｃ量（0.１０％〜0.１６％）およびＳｉ量
（0.２５％〜0.３８％）が高く、溶接部靱性を考慮すべ
きラインパイプ用鋼材としての充分な性能は確保できな
い。また、厚板圧延のため巻取温度についての配慮もな
されていない。Regarding the steel sheet manufacturing method disclosed in Japanese Patent Laid-Open No. 64-47815, ferrite + may be added depending on the conditions.
Although it is said that a two-phase structure of bainite is obtained, as far as the examples are seen, the C content (0.10% to 0.16%) and the Si content (0.25% to 0.38%) are high. Sufficient performance cannot be secured as a steel material for line pipes, where toughness should be considered. In addition, since the plate is rolled, no consideration is given to the winding temperature.
【００１６】[0016]
【作用】次に、本発明条件の限定理由を鋼成分、熱間圧
延条件の順で説明する。Next, the reasons for limiting the conditions of the present invention will be described in the order of steel composition and hot rolling conditions.
【００１７】（Ａ）鋼成分 Ｃ：鋼板の強度確保のため、0.０４％以上を必要とす
る。しかし、Ｃ量の増加は鋼板の靱性低下を招き、ま
た、周溶接ＨＡＺ部の靱性を低下させる。従って、Ｃの
上限を0.１０％（0.１０％は含まず）とした。(A) Steel composition C: 0.04% or more is required to secure the strength of the steel sheet. However, an increase in the amount of C causes a decrease in the toughness of the steel sheet and also a decrease in the toughness of the HAZ portion of the circumferential weld. Therefore, the upper limit of C is set to 0.10% (not including 0.10%).
【００１８】Ｓｉ：脱酸のために使用されるが、周溶接
ＨＡＺ部の靱性確保のためには少ないほうが良い。Ｍｏ
添加鋼ではＨＡＺ部に島状マルテンサイトが生成しやす
く、靱性確保の障害になる。この観点から、Ｓｉは0.０
３〜0.１５％とした。Si: Used for deoxidation, but should be as small as possible in order to secure the toughness of the HAZ portion of the peripheral weld. Mo
In the added steel, island martensite is likely to be formed in the HAZ portion, which becomes an obstacle to ensuring toughness. From this viewpoint, Si is 0.0
It was set to 3 to 0.15%.
【００１９】Ｍｎ：母材強度・靱性の確保の観点から一
定量の添加が必要であり、またＭｏの添加によりベイナ
イト組織を得るためにも下限を1.０％とした。過度の添
加は周溶接ＨＡＺ部の靱性を劣化させるため、上限を1.
６％とした。Mn: From the viewpoint of securing the strength and toughness of the base metal, it is necessary to add a certain amount, and in order to obtain a bainite structure by adding Mo, the lower limit was made 1.0%. Since excessive addition deteriorates the toughness of the HAZ part of the circumferential weld, the upper limit is 1.
It was 6%.
【００２０】Ｍｏ：変態強化、特にフェライト＋ベイナ
イト組織を生成させて低ＹＲ化を図るために、0.２０％
以上を必要とする。しかし、大量の添加は周溶接ＨＡＺ
部の靱性を低下させる原因になるので、その上限を0.３
０％とした。Mo: 0.20% for strengthening the transformation, especially for forming a ferrite + bainite structure to lower the YR.
You need more than that. However, a large amount of addition is perimeter welding HAZ
The upper limit is 0.3 because it causes deterioration of the toughness of the part.
It was set to 0%.
【００２１】Ｎｂ，Ｔｉ：結晶粒の細粒化および周溶接
ＨＡＺ部の靱性確保のために、いずれも0.０１０％以上
を必要とする。しかし、これらの元素が多くなると析出
強化に至り、母材靱性の劣化を招く。さらに過剰のＴｉ
は周溶接ＨＡＺ靱性を劣化させる。そこで、Ｎｂは0.０
５０％以下、Ｔｉは0.０３％以下に制限する。Nb, Ti: In order to make the crystal grains finer and to secure the toughness of the HAZ portion in the peripheral weld, both of them are required to be 0.010% or more. However, if these elements increase, precipitation strengthening will occur, resulting in deterioration of the toughness of the base material. Further excess Ti
Deteriorates the HAZ toughness of the circumferential weld. Therefore, Nb is 0.0
It is limited to 50% or less and Ti to 0.03% or less.
【００２２】不純物（Ｐ，Ｓ，Ｓｏｌ．Ａｌ）：Ｐ，Ｓ
は有害藤元素であり、靱性確保の為には低い方が好まし
い。しかし過度の低下は製鋼コストの増大を招くため、
Ｐ≦0.２０％，Ｓ≦0.０５％とした。Ａｌは脱酸剤であ
ると同時に窒化物（ＡｌＮ）を形成し、組織の微細化に
よる靱性改善に寄与するが、過度の添加はかえって靱性
を劣化させるため、0.０２０％〜0.０５０％とした。Impurities (P, S, Sol. Al): P, S
Is a harmful element and is preferably lower in order to secure toughness. However, excessive reduction causes an increase in steelmaking costs,
P ≦ 0.20% and S ≦ 0.05%. Al forms a nitride (AlN) at the same time as a deoxidizer, and contributes to the improvement of toughness due to the refinement of the structure, but excessive addition rather deteriorates toughness, so 0.020% to 0.050% And
【００２３】（Ｂ）熱間圧延条件 圧延仕上温度：圧延途中でのフェライトの析出は加工フ
ェライトを生じ、ＹＳの上昇によるＹＲの上昇を招く。
したがって、Ａｒ3 点以上で圧延を終了する必要があ
る。さらに、Ａｒ3 点以上でも十分な仕上温度が確保で
きない場合、加工オーステナイトによる強度の異方性を
生じ、板幅方向のＹＳ上昇によるＹＲの上昇を招くた
め、仕上温度は（Ａｒ3 ＋２０℃）以上とした。(B) Hot rolling conditions Rolling finishing temperature: Precipitation of ferrite during rolling produces worked ferrite, which causes an increase in YR due to an increase in YS.
Therefore, it is necessary to finish the rolling at the Ar 3 point or higher. Furthermore, if a sufficient finishing temperature cannot be secured even at Ar 3 points or more, strength anisotropy due to processed austenite occurs and YR rises due to YS rise in the plate width direction, so the finishing temperature is (Ar 3 + 20 ° C). That's it.
【００２４】圧延後の冷却：圧延後の初期冷却段階で十
分なフェライトを析出させＹＳの低下によるＹＲの低下
を確実なものとすべく、Ａｒ3 点より（Ａｒ3 −８０
℃）までの冷却速度は１０℃／秒以下が必要である。[0024] After rolling Cooling: In order to made reliable deterioration decrease in YR by the YS to precipitate sufficient ferrite in the initial cooling stage after rolling, than Ar 3 point (Ar 3 -80
The cooling rate up to (° C) is required to be 10 ° C / sec or less.
【００２５】巻取温度：フェライトが析出した後の第二
相組織をパーライト析出をおさえて微細なベイナイト組
織とすべく、十分な冷却を与えるため巻取温度は５００
℃以下とする必要がある。Winding temperature: The winding temperature is 500 in order to provide sufficient cooling so that the second phase structure after ferrite precipitation is suppressed to a fine bainite structure by suppressing pearlite precipitation.
It must be below ℃.
【００２６】[0026]
【実施例】以下に本発明の実施例を説明する。EXAMPLES Examples of the present invention will be described below.
【００２７】転炉にて溶製した鋼を連続鋳造にて幅１２
００ｍｍ×厚み２３０ｍｍのスラブとし、これを熱間圧
延にて厚み７ｍｍ又は１６ｍｍのコイルとした。その熱
延鋼板から板幅方向試片を採取して機械的性能を調査す
ると共に、周溶接性を評価すべく、鋼板の継手溶接（Ｍ
ＡＧ溶接：入熱約１０ｋＪ／ｃｍ）を行ない、ＨＡＺ部
の靱性を調査した。The width of the steel melted in the converter is 12 by continuous casting.
A slab having a thickness of 00 mm and a thickness of 230 mm was formed into a coil having a thickness of 7 mm or 16 mm by hot rolling. In order to evaluate the peripheral weldability, a joint welding of steel sheets (M
AG welding: A heat input of about 10 kJ / cm) was performed to examine the toughness of the HAZ part.
【００２８】鋼組成を表１に、熱延条件および試験結果
を表２に示すが、本発明法で製造された鋼板は、ライン
パイプ用鋼材として必要な性能、即ち低ＹＲ、高強度、
高靱性および高溶接性を全て合わせ持つ。The steel composition is shown in Table 1, and the hot rolling conditions and test results are shown in Table 2. The steel sheet produced by the method of the present invention has the properties required as a steel material for line pipes, that is, low YR and high strength.
It has both high toughness and high weldability.
【００２９】[0029]
【表１】 [Table 1]
【００３０】[0030]
【表２】 [Table 2]
【００３１】[0031]
【発明の効果】以上の説明から明らかなように、本発明
のラインパイプ用熱延鋼板の製造方法は、ラインパイプ
用鋼材として充分な強度靱性および周溶接性を確保し、
なおかつＹＲを低くできる。As is apparent from the above description, the method for producing a hot-rolled steel sheet for line pipes of the present invention ensures sufficient strength toughness and circumferential weldability as a steel material for line pipes,
Moreover, YR can be lowered.
【図１】強度および靱性に及ぼす各種合金元素の影響を
示す図表である。FIG. 1 is a chart showing the influence of various alloying elements on strength and toughness.
【図２】各種合金鋼のシーム熱処理部靱性を示す図表で
ある。FIG. 2 is a chart showing the toughness of seam heat treated parts of various alloy steels.
Claims (1)
満、Ｓｉ：0.０３〜0.１５％、Ｍｎ：1.０〜1.６％、Ｍ
ｏ：0.２０〜0.３０％、Ｎｂ：0.０１０〜0.０５％、Ｔ
ｉ：0.０１〜0.０３０％を含み、残部Ｆｅおよび不可避
不純物からなる鋼を、加熱後、（Ａｒ3 点＋２０℃）以
上の仕上温度で熱間圧延し、更に、（Ａｒ3 点−８０
℃）までの間を１０℃／秒以下の冷却速度で緩冷却し
て、５００℃以下の温度で巻き取ることを特徴とするラ
インパイプ用熱延鋼板の製造方法。1. A weight ratio of C: 0.04% or more and less than 0.10%, Si: 0.03 to 0.15%, Mn: 1.0 to 1.6%, M.
o: 0.20 to 0.30%, Nb: 0.010 to 0.05%, T
After heating, steel containing i: 0.01 to 0.030% and the balance Fe and unavoidable impurities is hot-rolled at a finishing temperature of (Ar 3 points + 20 ° C.) or higher, and further (Ar 3 points- 80
C.) is slowly cooled at a cooling rate of 10 [deg.] C./sec or less and is wound at a temperature of 500 [deg.] C. or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19928892A JPH0617125A (en) | 1992-07-01 | 1992-07-01 | Production of hot rolled steel plate for line pipe |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19928892A JPH0617125A (en) | 1992-07-01 | 1992-07-01 | Production of hot rolled steel plate for line pipe |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0617125A true JPH0617125A (en) | 1994-01-25 |
Family
ID=16405310
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19928892A Pending JPH0617125A (en) | 1992-07-01 | 1992-07-01 | Production of hot rolled steel plate for line pipe |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0617125A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100463736C (en) * | 2005-11-30 | 2009-02-25 | 鞍钢股份有限公司 | Production method capable of controlling pipeline steel hot rolling flat-board yield ratio |
| US8070887B2 (en) * | 2002-04-09 | 2011-12-06 | Nippon Steel Corporation | High-strength steel sheet and high-strength steel pipe excellent in deformability and method for producing the same |
| CN107723602A (en) * | 2017-11-23 | 2018-02-23 | 攀钢集团攀枝花钢铁研究院有限公司 | 750MPa levels hot-rolled ferrite-bainite dual-phase steel and its production method |
| CN113528933A (en) * | 2021-05-31 | 2021-10-22 | 武汉钢铁有限公司 | Hot continuous rolling complex phase high-strength steel and production method thereof |
| DE112005002484B4 (en) | 2004-10-08 | 2022-12-22 | The University Of Virginia Patent Foundation | Simultaneous sequence analysis of amino and carboxy end groups |
-
1992
- 1992-07-01 JP JP19928892A patent/JPH0617125A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8070887B2 (en) * | 2002-04-09 | 2011-12-06 | Nippon Steel Corporation | High-strength steel sheet and high-strength steel pipe excellent in deformability and method for producing the same |
| DE112005002484B4 (en) | 2004-10-08 | 2022-12-22 | The University Of Virginia Patent Foundation | Simultaneous sequence analysis of amino and carboxy end groups |
| CN100463736C (en) * | 2005-11-30 | 2009-02-25 | 鞍钢股份有限公司 | Production method capable of controlling pipeline steel hot rolling flat-board yield ratio |
| CN107723602A (en) * | 2017-11-23 | 2018-02-23 | 攀钢集团攀枝花钢铁研究院有限公司 | 750MPa levels hot-rolled ferrite-bainite dual-phase steel and its production method |
| CN113528933A (en) * | 2021-05-31 | 2021-10-22 | 武汉钢铁有限公司 | Hot continuous rolling complex phase high-strength steel and production method thereof |
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