JPH05261567A - Manufacture of clad steel plate having excellent low temperature toughness - Google Patents
Manufacture of clad steel plate having excellent low temperature toughnessInfo
- Publication number
- JPH05261567A JPH05261567A JP4991692A JP4991692A JPH05261567A JP H05261567 A JPH05261567 A JP H05261567A JP 4991692 A JP4991692 A JP 4991692A JP 4991692 A JP4991692 A JP 4991692A JP H05261567 A JPH05261567 A JP H05261567A
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- Prior art keywords
- rolling
- temperature
- base material
- toughness
- steel
- Prior art date
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- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は合わせ材として、ステン
レス鋼あるいはニッケル合金などの耐食性の優れた高合
金を、母材として特定の低合金鋼（低Ｃ−Ｍｎ−高Ｎｂ
−微量Ｔｉ）を使用し、圧延ままで耐食性の優れたクラ
ッド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 uses a high alloy with excellent corrosion resistance such as stainless steel or nickel alloy as a base material and a specific low alloy steel (low C--Mn--high Nb) as a base material.
-A small amount of Ti) and a method for producing a clad steel sheet having excellent corrosion resistance as rolled.
【０００２】[0002]
【従来の技術】安全性、経済性の観点から腐食性物質
（Ｈ2 Ｓ，ＣＯ2 ，Ｃｌ- ）を多く含有する原油・天然
ガス輸送用大径ラインパイプに、ステンレス鋼やニッケ
ル合金を合わせ材とする高合金クラッド鋼管の採用が増
加しつつある。従来、このような鋼管は圧延クラッド鋼
板を成形（ＵＯＥ成形）、シーム溶接後、鋼管全体を再
加熱・冷却（溶体化処理）することにより製造されてい
たが、最近、溶体化処理を省略し圧延ままで目標とする
特性を達成する技術が開発されている（例えば特開昭６
０−２１６９８４号公報、特開昭６２−１６８９２号公
報、特開昭６３−１３０２８３号公報）。2. Description of the Related Art From the viewpoint of safety and economy, a stainless steel or nickel alloy is combined with a large-diameter line pipe for transporting crude oil / natural gas containing a large amount of corrosive substances (H 2 S, CO 2 , Cl − ). The adoption of high alloy clad steel pipes as a material is increasing. Conventionally, such a steel pipe has been manufactured by forming a rolled clad steel plate (UOE forming), seam welding, and then reheating and cooling the entire steel pipe (solution treatment), but recently, the solution treatment has been omitted. Techniques have been developed to achieve the target characteristics in the as-rolled state (for example, Japanese Patent Laid-Open No. Sho 6).
0-216984, JP-A-62-16892, JP-A-63-130283).
【０００３】しかし、これらの方法では圧延ままで合わ
せ材の優れた耐食性、母材の強度・低温靭性を得ること
はきわめて困難である。これは、「合わせ材の耐食性は
高温（９００℃以上）で圧延するほど向上し、一方、母
材の低温靭性は低温で圧延するほど向上する」などの理
由による。その結果、従来の技術では圧延温度の低下が
強いられ、クラッド鋼板の耐食性が犠牲にされる側面が
あった。However, with these methods, it is extremely difficult to obtain excellent corrosion resistance of a laminated material and strength / low temperature toughness of a base material as they are rolled. This is because the corrosion resistance of the laminated material is improved as it is rolled at a higher temperature (900 ° C. or higher), while the low temperature toughness of the base material is improved as it is rolled at a lower temperature. As a result, in the conventional technique, the rolling temperature is forced to decrease, and the corrosion resistance of the clad steel sheet is sacrificed.
【０００４】[0004]
【発明が解決しようとする課題】本発明は圧延まま高合
金クラッド鋼板の製造（区間の溶体化処理の省略）にお
いて、優れた合わせ材の耐食性と母材の強度・低温靭性
を同時に達成できる製造方法を提供するものである。DISCLOSURE OF THE INVENTION According to the present invention, in the production of an as-rolled high alloy clad steel sheet (omission of solution treatment in the section), excellent corrosion resistance of a laminated material and strength / low temperature toughness of a base material can be simultaneously achieved. It provides a method.
【０００５】[0005]
【課題を解決するための手段】本発明の要旨は、ステン
レス鋼またはニッケル合金からなる合わせ材と、重量％
でＣ：０．０２〜０．０６、Ｓｉ：０．５以下、Ｍｎ：
１．０〜１．８、Ｐ：０．０３以下、Ｓ：０．００５以
下、Ｎｂ：０．０８〜０．１５、Ｔｉ：０．００５〜
０．０３、Ａｌ：０．０５以下、Ｎ：０．００２〜０．
００６に必要に応じて、さらにＮｉ：０．０５〜１．
０、Ｃｕ：０．０５〜１．０、Ｃｒ：０．０５〜０．
５、Ｍｏ：０．０５〜０．３、Ｃａ：０．００１〜０．
００５の１種または２種以上を含有し、残部が鉄および
不可避的不純物からなる鋼母材とを重ね合わせて四周を
溶接してスラブを組み立て、これを１１００〜１２５０
℃の温度範囲に加熱後、１０００℃を超える温度から圧
延を開始し、１０００℃以下での圧下比を３以上、総圧
下比を５以上として、圧延終了温度９００〜１０００℃
で圧延し、３０〜２００秒間空冷した後、７５０℃以上
の温度から５〜４０℃／秒の冷却速度で５５０℃以下の
任意の温度まで冷却、その後空冷することを特徴とする
低温靭性の優れたクラッド鋼板の製造方法である。SUMMARY OF THE INVENTION The gist of the present invention is to provide a laminated material made of stainless steel or a nickel alloy, and
C: 0.02-0.06, Si: 0.5 or less, Mn:
1.0-1.8, P: 0.03 or less, S: 0.005 or less, Nb: 0.08-0.15, Ti: 0.005-
0.03, Al: 0.05 or less, N: 0.002 to 0.
006, Ni: 0.05-1.
0, Cu: 0.05 to 1.0, Cr: 0.05 to 0.
5, Mo: 0.05 to 0.3, Ca: 0.001 to 0.
A steel slab containing at least one of 005 and a balance of iron and unavoidable impurities is superposed on each other and welded on four sides to assemble a slab.
After heating to a temperature range of 1000C, rolling is started from a temperature exceeding 1000C, and the rolling reduction temperature at 1000C or less is set to 3 or more, the total rolling ratio is 5 or more, and the rolling end temperature is 900 to 1000C.
Excellent in low-temperature toughness, characterized in that it is cooled at a temperature of 750 ° C. or higher to an arbitrary temperature of 550 ° C. or lower at a cooling rate of 5 to 40 ° C./sec, and then air-cooled. It is a method of manufacturing a clad steel plate.
【０００６】本発明のステンレス鋼とは、オーステナイ
ト系、フェライト系、マルテンサイト系および２相系を
指し、ニッケル合金とはインコロイ８２５、インコネル
６２５などであり、耐食性の優れた材料である。また、
母材はその特性（圧延方向と直角方向での値）が強度Ｘ
５２以上（ＡＰＩ規格）、低温靭性ｖＥ-30 ≧１０kgｆ
−ｍ，ｖＴｒｓ≦−６０℃となるような高強度、高靭性
の低合金鋼である。[0006] The stainless steel of the present invention refers to austenitic, ferritic, martensitic and two-phase, and nickel alloys such as Incoloy 825 and Inconel 625, which are materials having excellent corrosion resistance. Also,
The strength of the base material is X (the value in the direction perpendicular to the rolling direction).
52 or more (API standard), low temperature toughness vE -30 ≧ 10 kgf
It is a low-alloy steel with high strength and high toughness such that −m, vTrs ≦ −60 ° C.
【０００７】本発明では、２つの方法でスラブを組み立
てる。第１の方法は母材１の表面に合わせ材２を重ね合
わせ四周を溶接してスラブを組み立てる。この際、母材
および合わせ材の接着面はあらかじめ研磨などによって
平滑にし、脱脂などによる清浄化や真空ポンプによる脱
気を行なうことが好ましい。第２の方法は第１の方法で
組み立てた２つのスラブの合わせ材を、分離材を介して
密着させ、四周を溶接してスラブ（サンドイッチスラ
ブ）を組み立てる方法である。In the present invention, the slab is assembled in two ways. The first method is to assemble the slab by superposing the joining material 2 on the surface of the base material 1 and welding the four circumferences. At this time, it is preferable that the adhering surfaces of the base material and the laminated material are smoothed in advance by polishing or the like, cleaning is performed by degreasing, or deaeration is performed by a vacuum pump. The second method is a method of assembling a slab (sandwich slab) by bringing the laminated materials of the two slabs assembled by the first method into close contact with each other via a separating material and welding the four circumferences.
【０００８】[0008]
【作用】以下本発明について詳細に説明する。本発明鋼
の特徴は、母材成分を低Ｃ−高Ｎｂ−微量Ｔｉ系とし、
１０００℃以下での圧下比を３以上とすることで、高温
で圧延を終了しても、合わせ材の優れた耐食性と母材の
優れた強度・靭性を同時に達成できるところにある。The present invention will be described in detail below. The feature of the steel of the present invention is that the base metal component is low C-high Nb-trace Ti system,
By setting the reduction ratio at 1000 ° C. or less to 3 or more, it is possible to achieve excellent corrosion resistance of the laminated material and excellent strength / toughness of the base material at the same time even when rolling is completed at a high temperature.
【０００９】合わせ材において優れた耐食制を得るに
は、再加熱時に合金元素を溶体化、これを高温で圧延、
適当な時間空冷してオーステナイト（γ）組織を再結晶
させ、かつ圧延後、急冷してσ相（Ｃｒ炭化物）などの
析出を抑制しなければならない。しかしながら、合わせ
材のγ組織が再結晶するような高温で圧延を行なうと、
母材の結晶粒の微細化が不十分となり、ラインパイプと
して十分な低温靭性を得ることができない。In order to obtain an excellent corrosion resistance in the laminated material, the alloy elements are solution-heated at the time of reheating, and this is rolled at a high temperature.
The austenite (γ) structure must be recrystallized by air cooling for an appropriate time, and after rolling, it must be rapidly cooled to suppress precipitation of the σ phase (Cr carbide) and the like. However, when rolling at a high temperature such that the γ structure of the laminated material recrystallizes,
The refinement of the crystal grains of the base material becomes insufficient, and sufficient low temperature toughness cannot be obtained as a line pipe.
【００１０】発明者らの一部はすでに、特願平２−３２
８３１０号明細書において母材成分を低Ｃ−高Ｎｂ−微
量Ｔｉ系とすることで、高温で圧延を終了しても良好な
強度・靭性が得られることを発明した。しかしながら、
圧延温度域を適正化すればさらに良好な強度・靭性が得
られることが判明し、適正な圧延条件について鋭意検討
した。その結果、低Ｃ−高Ｎｂ−微量Ｔｉ系において１
０００℃を超える温度から圧延を開始し、１０００℃以
下での圧下比を３以上とすることにより、極めて良好な
低温靭性が得られることを見い出した。高Ｎｂ鋼につい
ては研究された例はあるが、クラッド鋼板への応用につ
いて、各温度域での圧下比も含めた研究・適用の例はな
い。Some of the inventors have already filed Japanese Patent Application No. 2-32.
In the specification of No. 8310, it has been invented that the base material component is a low C-high Nb-trace Ti system, and good strength and toughness can be obtained even when rolling is completed at high temperature. However,
It was found that even better strength and toughness can be obtained by optimizing the rolling temperature range, and the inventors conducted diligent studies on appropriate rolling conditions. As a result, in the low C-high Nb-trace Ti system, 1
It has been found that extremely good low temperature toughness can be obtained by starting the rolling from a temperature exceeding 000 ° C and setting the reduction ratio at 1000 ° C or lower to 3 or more. Although there is an example of research on high Nb steel, there is no example of research and application including application of reduction ratio in each temperature range to clad steel plate.
【００１１】まず、本発明の再加熱温度・圧延冷却条件
について説明する。本発明では、上記の組み立てスラブ
を１１００〜１２５０℃の範囲に再加熱する。これは合
わせ材の耐食性と母材の強度・靭性を同時に確保するた
め必要である。下限温度１１００℃は、合わせ材の優れ
た耐食性を得るために十分に溶体化し、圧延終了温度を
９００℃以上として圧延後、合わせ材のγ組織を再結晶
させるのに必要な最低加熱温度である。しかし、再加熱
温度が１２５０℃以上になると、母材の結晶粒が微細化
せず低温靭性の劣化を招く。したがって、適切な再加熱
温度は１１００〜１２５０℃である。First, the reheating temperature and rolling cooling conditions of the present invention will be described. In the present invention, the above assembled slab is reheated to the range of 1100-1250 ° C. This is necessary to ensure the corrosion resistance of the laminated material and the strength and toughness of the base material at the same time. The lower limit temperature of 1100 ° C. is a minimum heating temperature necessary for resolving the γ structure of the laminated material after solution rolling sufficiently to obtain excellent corrosion resistance of the laminated material and rolling at a rolling end temperature of 900 ° C. or higher. .. However, when the reheating temperature is 1250 ° C. or higher, the crystal grains of the base material do not become fine and the low temperature toughness deteriorates. Therefore, a suitable reheating temperature is 1100 to 1250 ° C.
【００１２】本発明における特定温度域での圧下条件
は、組織の微細化による母材低温靭性の改善に極めて重
要な要件である。再加熱したスラブは１０００℃を超え
る温度から圧延を開始されなければならず、この時１０
００℃を超える温度域での圧下比を１．５以上とするこ
とが好ましい。この理由は、母材γ組織を１０００℃を
超える再結晶温度域で圧延することによって、γ粒の微
細化および整粒化をはかるためであり、圧下比を１．５
以上とすることは母材γ組織の再結晶による微細化およ
び整粒化により効果的である。The rolling condition in the specific temperature range in the present invention is a very important requirement for improving the low temperature toughness of the base material by refining the structure. The reheated slab must be rolled at a temperature above 1000 ° C, at which time 10
It is preferable that the reduction ratio in the temperature range exceeding 00 ° C. is 1.5 or more. The reason for this is that by rolling the base material γ structure in a recrystallization temperature range of more than 1000 ° C., the γ grains are made finer and the grain size is controlled, and the reduction ratio is 1.5.
The above is effective for refining and grain size control by recrystallization of the base metal γ structure.
【００１３】続いて１０００℃以下での圧下比が３以上
となるように圧延されなければならない。この理由は、
母材γ組織を１０００℃以下の未再結晶温度域で強圧下
することによってγ粒の伸延化、γ粒内への加工歪
の導入をはかり、γ→α変態時の核生成サイトであるγ
粒界や加工歪を増加させることでより、微細な母材最終
組織を得るためである。１０００℃以下での圧下比が３
未満であると、γ粒の伸延化が不十分なためにγ→α変
態時の核生成サイトであるγ粒界の面積が少なく、同様
に核生成サイトであるγ粒内の加工歪量も少ないため
に、変態後の母材最終組織は十分な微細化がなされず、
優れた母材低温靭性は得られない。Subsequently, it must be rolled so that the rolling reduction ratio at 1000 ° C. or lower becomes 3 or higher. The reason for this is
By strongly reducing the γ structure of the base material in the unrecrystallized temperature range of 1000 ° C. or less, elongation of γ grains and introduction of processing strain into γ grains are attempted, and γ is a nucleation site during the γ → α transformation.
This is to obtain a finer final matrix microstructure by increasing grain boundaries and processing strain. Reduction ratio below 1000 ℃ is 3
If it is less than, the area of the γ grain boundary that is a nucleation site during the γ → α transformation is small because the elongation of the γ grain is insufficient, and similarly the amount of processing strain in the γ grain that is the nucleation site is also small. Due to the small amount, the final structure of the base material after transformation is not sufficiently refined,
Excellent low temperature toughness of the base material cannot be obtained.
【００１４】また、総圧下比を５以上とする理由は、合
わせ材と母材を冶金的に完全に密着させるためである。
したがって、総圧下比は大きいほど好ましい。最低総圧
下比は再加熱温度や圧延温度にも依存するが、本発明の
ように圧延温度が高い場合５以上である。The reason why the total rolling reduction ratio is 5 or more is that the laminated material and the base material are completely metallurgically adhered to each other.
Therefore, the larger the total reduction ratio, the more preferable. The minimum total reduction ratio depends on the reheating temperature and the rolling temperature, but is 5 or more when the rolling temperature is high as in the present invention.
【００１５】本発明では、圧延終了温度を９００℃〜１
０００℃の範囲としている。圧延終了温度が９００℃未
満であると、著しく劣化する。合わせ材の耐食性の観点
からは圧延終了温度は高いほど好ましい。しかし圧延終
了温度が高過ぎると母材の結晶粒が微細化せず、低温靭
性の劣化を招く。このため圧延終了温度を１０００℃以
下に限定した。In the present invention, the rolling end temperature is 900 ° C to 1
The range is 000 ° C. If the rolling end temperature is lower than 900 ° C, the rolling will be significantly deteriorated. From the viewpoint of the corrosion resistance of the laminated material, the higher the rolling end temperature is, the more preferable. However, if the rolling end temperature is too high, the crystal grains of the base material do not become fine and the low temperature toughness deteriorates. Therefore, the rolling end temperature is limited to 1000 ° C or lower.
【００１６】さらに本発明では、圧延終了後３０〜２０
０秒間冷却し、７５０℃以上の温度から５〜４０℃／秒
の冷却速度で５５０℃以下の任意の温度まで冷却、その
後空冷する。圧延後に空冷時間を設ける理由は、合わせ
材のγ組織の再結晶を促進させ、耐食性を改善するため
である。圧延直後に急冷すると良好な耐食性は得られな
い。Further, in the present invention, 30 to 20 after the rolling is completed.
Cooling for 0 seconds, cooling from a temperature of 750 ° C. or higher to an arbitrary temperature of 550 ° C. or lower at a cooling rate of 5 to 40 ° C./second, and then air cooling. The reason for providing the air cooling time after rolling is to accelerate the recrystallization of the γ structure of the laminated material and improve the corrosion resistance. If it is cooled immediately after rolling, good corrosion resistance cannot be obtained.
【００１７】圧延終了温度が９００℃以上の場合、最低
３０秒の空冷時間が必要である（望ましくは６０秒以
上）。しかし空冷時間の延長はクラッド鋼板の温度低下
を招き、σ相（Ｃｒ炭化物）などの析出を生じさせる。
または加速冷却による母材の強靭化にも支障をきたす。
このため鋼板の厚みにも依存するが、空冷時間は２００
秒以下とし、かつ７５０℃以上の温度から水冷しなけれ
ばならない。このとき、σ相（Ｃｒ炭化物）の析出を
抑制し、加速冷却による母材の強靭化をはかるために
は、冷却条件として冷却速度５〜４０℃／秒で５５０℃
以下まで冷却する必要がある。なお、圧延後のクラッド
鋼板を低温靭性改善、脱水素などの目的でＡｃ1 以下の
温度に再加熱（焼戻処理）することは、何ら本発明の特
徴を損なうものではない。When the rolling end temperature is 900 ° C. or higher, an air cooling time of at least 30 seconds is required (desirably 60 seconds or longer). However, the extension of the air-cooling time causes the temperature of the clad steel sheet to drop, and causes the precipitation of σ phase (Cr carbide) and the like.
Alternatively, it also hinders the strengthening of the base material by accelerated cooling.
Therefore, depending on the thickness of the steel sheet, the air cooling time is 200
It must be water-cooled at a temperature of 750 ° C or higher for less than 2 seconds. At this time, in order to suppress the precipitation of the σ phase (Cr carbide) and to strengthen the base material by accelerated cooling, the cooling condition is 550 ° C at a cooling rate of 5 to 40 ° C / sec.
It is necessary to cool to the following. Reheating (tempering) the clad steel sheet after rolling to a temperature of Ac 1 or lower for the purpose of improving low temperature toughness, dehydrogenation, etc. does not impair the characteristics of the present invention.
【００１８】つぎに本発明の母材成分の限定理由につい
て説明する。母材の強度・靭性および合わせ材の耐食性
を確保するために、Ｃ，Ｍｎ，Ｎｂ，Ｔｉ量をそれぞれ
重量％で、０．０２〜０．０６，１．０〜１．８，０．
０８〜０．１５，０．００５〜０．０３に限定する。
Ｃ，Ｍｎ量の下限は、Ｎｂ添加による析出硬化、結晶粒
微細化効果によって、母材および溶接部が目的とする強
度・靭性を確保するための最小量である。また上限は母
材の優れた低温靭性・現地溶接性を得るための限界値で
ある。母材Ｃ量が高過ぎると組み立てスラブの再加熱時
に母材のＣが合わせ材へ拡散し、耐食性が劣化する。し
たがって、合わせ材の耐食性の面からも母材のＣ量を
０．０６％以下に制限する必要がある。Next, the reasons for limiting the base material components of the present invention will be explained. In order to secure the strength and toughness of the base material and the corrosion resistance of the laminated material, the amounts of C, Mn, Nb, and Ti are 0.02 to 0.06, 1.0 to 1.8, and 0.0.
It is limited to 08 to 0.15 and 0.005 to 0.03.
The lower limits of the amounts of C and Mn are the minimum amounts for securing the desired strength and toughness of the base material and the welded portion by the precipitation hardening and crystal grain refining effects due to the addition of Nb. The upper limit is a limit value for obtaining excellent low temperature toughness and field weldability of the base material. If the amount of base metal C is too high, C of the base metal diffuses into the laminated material when the assembled slab is reheated, and the corrosion resistance deteriorates. Therefore, it is necessary to limit the C content of the base material to 0.06% or less in terms of the corrosion resistance of the laminated material.
【００１９】本発明鋼では必須の元素としてＮｂ：０．
０８〜０．１５％、Ｔｉ：０．００５〜０．０３％を含
有させる。Ｎｂは制御圧延において結晶粒の微細化や析
出硬化に寄与し、鋼を強靭化する効果を有する。合わせ
材の耐食性のため、９００℃以上の高温で圧延を終了し
なければならない本発明鋼においては、Ｎｂは最低０．
０８％以上添加する必要がある。これによって本発明の
ように高温圧延を基本とする特殊な製造条件においても
結晶粒の微細化や析出硬化が進行し、従来のクラッド鋼
板に比較して優れた強度・靭性が得られる。しかしＮｂ
を０．１５％以上添加すると現地溶接性や溶接部靭性が
劣化するのでその上限を０．１５％とした。In the steel of the present invention, Nb: 0.
08-0.15% and Ti: 0.005-0.03% are contained. Nb contributes to grain refinement and precipitation hardening in controlled rolling, and has the effect of strengthening the steel. Due to the corrosion resistance of the laminated material, Nb is at least 0.
It is necessary to add 08% or more. As a result, the refinement of crystal grains and precipitation hardening proceed even under special manufacturing conditions based on high temperature rolling as in the present invention, and excellent strength and toughness can be obtained as compared with conventional clad steel sheets. But Nb
If 0.15% or more is added, on-site weldability and weld zone toughness deteriorate, so the upper limit was made 0.15%.
【００２０】またＴｉ添加は微細なＴｉＮを形成し、ス
ラブ再加熱時や溶接時にγ粒の粗大化を抑制し、母材靭
性、溶接熱影響部（ＨＡＺ）靭性の改善に効果がある。
この効果は高温で圧延する本発明鋼においては特に重要
である。ＴｉＮの効果を十分に発揮させるには最低０．
００５％のＴｉ添加が必要である。しかしＴｉ量が多過
ぎるとＴｉＮの粗大化やＴｉＣによる析出硬化が起こ
り、低温靭性が劣化するので、その上限は０．０３％に
制限する必要がある。The addition of Ti forms fine TiN, suppresses the coarsening of γ grains during slab reheating and welding, and is effective in improving the toughness of the base material and the weld heat affected zone (HAZ).
This effect is particularly important in the steel of the present invention rolled at a high temperature. In order to fully bring out the effect of TiN, at least 0.
005% Ti addition is required. However, if the Ti amount is too large, coarsening of TiN or precipitation hardening due to TiC will occur and the low temperature toughness will deteriorate, so the upper limit must be limited to 0.03%.
【００２１】つぎにその他の元素の限定理由について説
明する。Ｓｉは鋼を強靭化させる元素であるが、多く添
加すると溶接性、ＨＡＺ靭性を劣化させるため、上限を
０．５％とした。鋼の脱酸はＴｉのみでも十分であり、
Ｓｉは必ずしも添加する必要はない。Next, the reasons for limiting other elements will be described. Si is an element that strengthens the steel, but if added in a large amount, it deteriorates the weldability and HAZ toughness, so the upper limit was made 0.5%. Ti alone is sufficient for deoxidizing steel,
Si does not necessarily have to be added.
【００２２】本発明鋼において不純物であるＰ，Ｓをそ
れぞれ０．０３％、０．００５％以下とした理由は母
材、溶接部の低温靭性をより一層向上させるためであ
る。Ｐ量の低減は粒界破壊を防止し、Ｓ量の低減はＭｎ
Ｓによる靭性の劣化を防止する。好ましいＰ，Ｓ量はそ
れぞれ０．０１，０．００３％以下である。The reason why the impurities P and S in the steel of the present invention are 0.03% and 0.005% or less, respectively, is to further improve the low temperature toughness of the base material and the welded portion. Reduction of P content prevents intergranular fracture, and reduction of S content is Mn.
Prevents deterioration of toughness due to S. The preferred P and S contents are 0.01 and 0.003% or less, respectively.
【００２３】Ａｌは通常脱酸剤として鋼に含まれる元素
であるが、脱酸はＴｉあるいはＳｉでも可能であり、必
ずしも添加する必要はない。Ａｌ量が０．０５％以上に
なるとＡｌ系非金属介在物が増加して鋼の清浄度が害す
るので、上限を０．０５％とした。Al is an element usually contained in steel as a deoxidizing agent, but deoxidizing can be performed with Ti or Si, and it is not always necessary to add it. When the amount of Al is 0.05% or more, Al-based nonmetallic inclusions increase and the cleanliness of steel is impaired, so the upper limit was made 0.05%.
【００２４】ＮはＴｉＮを形成しγ粒の粗大化抑制効果
を通じて母材靭性、ＨＡＺ靭性を向上させる。このため
の最小量は０．００２％である。しかし多過ぎるとスラ
ブ表面疵や固溶ＮによるＨＡＺ靭性の劣化原因となるの
で、その上限は０．００６％以下に抑える必要がある。N forms TiN and improves the base material toughness and HAZ toughness through the effect of suppressing the coarsening of γ grains. The minimum amount for this is 0.002%. However, if it is too large, it will cause deterioration of the HAZ toughness due to slab surface defects and solid solution N, so the upper limit must be suppressed to 0.006% or less.
【００２５】つぎにＮｉ，Ｃｕ，Ｃｒ，Ｍｏ，Ｃａを添
加する理由について説明する。基本となる成分にこれら
の元素を添加する主たる目的は、本発明鋼の優れた特徴
を損なうことなく母材の強度・靭性などの特性向上をは
かるためである。したがってその添加量は自ずから制限
される性質のものである。Next, the reason for adding Ni, Cu, Cr, Mo and Ca will be explained. The main purpose of adding these elements to the basic components is to improve the properties such as strength and toughness of the base metal without impairing the excellent characteristics of the steel of the present invention. Therefore, the added amount is naturally limited.
【００２６】Ｎｉは溶接性、ＨＡＺ靭性に悪影響をおよ
ぼすことなく強度・靭性をともに向上させるほか、Ｃｕ
添加時の熱間割れ防止にも効果がある。しかし１．０％
を超えると経済性の点で好ましくないため、その上限を
１．０％とした。Ni improves both strength and toughness without adversely affecting weldability and HAZ toughness, and Cu
It is also effective in preventing hot cracking during addition. But 1.0%
Since it is not preferable from the viewpoint of economical efficiency, the upper limit was made 1.0%.
【００２７】Ｃｕは耐食性、耐水素誘起割れ性に効果が
あるが、１．０％を超えると熱間圧延時にＣｕ−クラッ
クが生じ製造が困難になる。このため上限を１．０％と
した。Ｃｒ，Ｍｏはともに強度の向上に効果がある。し
かし多く添加すると溶接性やＨＡＺ靭性を害するので、
その上限をそれぞれ０．５，０．３％とした。なおＮ
ｉ，Ｃｕ，Ｃｒ，Ｍｏの下限０．００５％は、これらの
元素の添加による材質上の効果を得るための最小量であ
る。Cu has an effect on the corrosion resistance and the resistance to hydrogen-induced cracking, but if it exceeds 1.0%, Cu-cracks are generated during hot rolling, which makes manufacture difficult. Therefore, the upper limit is set to 1.0%. Both Cr and Mo are effective in improving strength. However, if a large amount is added, the weldability and HAZ toughness are impaired, so
The upper limits were set to 0.5 and 0.3%, respectively. N
The lower limit of 0.005% of i, Cu, Cr and Mo is the minimum amount for obtaining the material effect by the addition of these elements.
【００２８】Ｃａは硫化物（ＭｎＳ）の形態を制御し、
低温靭性を向上させる（シャルピー吸収エネルギーの増
加など）ほか、耐水素誘起割れ性の改善にも著しい効果
を発揮する。しかしＣａ量が０．００１％以下では実用
上効果はなく、また０．００５％以上添加するとＣａ
Ｏ，ＣａＳが大量に生成して大型介在物を形成し、鋼の
清浄度を害するだけでなく、靭性、現地溶接性に悪影響
をおよぼす。このためＣａ添加量を０．００１〜０．０
０５％に制限した。Ca controls the morphology of sulfide (MnS),
In addition to improving low temperature toughness (increasing Charpy absorbed energy, etc.), it also exerts a remarkable effect in improving hydrogen-induced cracking resistance. However, if the amount of Ca is less than 0.001%, there is no practical effect, and if more than 0.005% is added, Ca
A large amount of O and CaS are formed to form large inclusions, which not only impairs the cleanliness of steel, but also adversely affects toughness and field weldability. Therefore, the amount of Ca added is 0.001 to 0.0.
Limited to 05%.
【００２９】なお、耐水素誘起割れ性の改善にはＳ，Ｏ
量をそれぞれ０．００１，０．００２％以下に低減し、
ＭｎＳの形態制御に有効なＣａ量とＳ量とのバランスを
表わす指標であるＥＳＳＰ（Ｅｆｆｅｃｔｉｖｅ ｓｕ
ｌｐｈｉｄｅ ｓｈａｐｅｃｏｎｔｒｏｌｌｉｎｇ ｐ
ａｒａｍｅｔｅｒ）を ＥＳＳＰ＝（Ｃａ）〔１−１２４（Ｏ）〕／１．２５（Ｓ）≧１ とすることが特に有効である。In order to improve the hydrogen-induced cracking resistance, S, O
The amount is reduced to 0.001, 0.002% or less,
ESSP (Effective su), which is an index representing the balance between the amount of Ca and the amount of S, which is effective in controlling the morphology of MnS.
lphide shapecontrolling p
It is particularly effective to set the parameter as ESSP = (Ca) [1-124 (O)] / 1.25 (S) ≧ 1.
【００３０】本発明は厚板ミルに適用することが最も好
ましいが、ホットコイルにも適用できる。また、この方
法で製造した鋼板は低温靭性、現地溶接性に優れている
ので、寒冷地におけるラインパイプに最も適する。The present invention is most preferably applied to thick plate mills, but can also be applied to hot coils. Further, the steel sheet produced by this method is excellent in low temperature toughness and field weldability, and is therefore most suitable for a line pipe in cold regions.
【００３１】[0031]
【実施例】転炉−連続鋳造で種々の鋼成分を母材スラブ
（厚み２４０mm）を製造した。このスラブを所定の厚み
に圧延した後、スラブの片表面を機械的に平削し、種々
の厚みのステンレス鋼（ＳＵＳ３１６Ｌ）またはインコ
ロイ８２５合わせ材（圧延後の鋼板の合わせ材厚みが３
mmになるように調整）と重ねて四周を溶接した。さら
に、このようにして製造したスラブ２枚の合わせ材を分
離材を介して重ね合わせ、四周を溶接してサンドイッチ
スラブを組み立てた。なお、接着面はすべて平滑にする
とともに、汚れを除去、脱脂し、空気を真空ポンプで除
去した。EXAMPLE A base metal slab (having a thickness of 240 mm) was produced by various steel components by a converter-continuous casting. After rolling this slab to a predetermined thickness, one surface of the slab is mechanically planed, and stainless steel (SUS316L) of various thicknesses or Incoloy 825 laminated material (the laminated material thickness of the rolled steel sheet is 3
(adjusted to be mm) and welded the four laps. Furthermore, the sandwich slabs were assembled by stacking the two laminated slabs manufactured in this way with a separator interposed therebetween and welding the four circumferences. In addition, all the adhered surfaces were made smooth, dirt was removed and degreased, and air was removed by a vacuum pump.
【００３２】種々の条件でサンドイッチスラブを再加熱
・圧延・冷却してクラッド鋼板を製造し、母材の強度・
靭性（シャルピー衝撃試験）、合わせ材の耐食性（孔食
の有無で評価、試験条件：１０％ＦｅＣｌ3 ・６Ｈ2 Ｏ
溶液にＳＵＳ３１６Ｌは１５℃で４８時間、インコロイ
８２５は３０℃で４８時間浸漬、母材と合わせ材の密着
性（超音波による探傷）を調査した。The sandwich slab is reheated, rolled and cooled under various conditions to produce a clad steel plate, and the strength of the base metal
Toughness (Charpy impact test), evaluated by the presence or absence of corrosion resistance of the cladding material (pitting, test conditions: 10% FeCl 3 · 6H 2 O
SUS316L was immersed in the solution at 15 ° C. for 48 hours, and Incoloy 825 was immersed at 30 ° C. for 48 hours, and the adhesion between the base material and the laminated material (inspection by ultrasonic waves) was investigated.
【００３３】表１に化学成分、製造条件、母材の特性、
密着性、耐食性を示す。Table 1 shows the chemical composition, manufacturing conditions, characteristics of the base material,
Shows adhesion and corrosion resistance.
【００３４】[0034]
【表１】 [Table 1]
【００３５】[0035]
【表２】 [Table 2]
【００３６】[0036]
【表３】 [Table 3]
【００３７】[0037]
【表４】 [Table 4]
【００３８】[0038]
【表５】 [Table 5]
【００３９】[0039]
【表６】 [Table 6]
【００４０】本発明法にしたがって製造したクラッド鋼
板（鋼１〜１０）は、母材、合わせ材ともすべて良好な
特性を有する。特に母材の低温靭性が優れており、シャ
ルピー衝撃試験よりもより厳しいＤＷＴＴにおいても良
好な低温靭性を示す。これに対して本発明によらない比
較鋼（鋼１１〜３０）は、母材、合わせ材の特性が劣
る。The clad steel plates (steels 1 to 10) produced according to the method of the present invention have good characteristics in both the base material and the laminated material. In particular, the low temperature toughness of the base material is excellent, and good low temperature toughness is exhibited even in DWTT, which is more severe than in the Charpy impact test. On the other hand, the comparative steels (Steels 11 to 30) not according to the present invention are inferior in the characteristics of the base material and the laminated material.
【００４１】鋼１１はＣ量が高くＭｎ量が低いため、低
温靭性が劣る。鋼１２はＳｉ，Ｍｎ量が高いため、強度
は良好であるが低温靭性が劣る。鋼１３はＮｂ量が低い
ため、鋼１４はＴｉが添加されていないため、鋼１５は
Ｎ量が低いため、鋼１６はＮ量が高いため、低温靭性が
劣る。鋼１７は再加熱温度が高いため、低温靭性が劣
る。鋼１８は再加熱温度が低いため、強度、合わせ材と
母材の密着性、耐食性が劣る。鋼１９〜２２は１０００
℃以上の圧下比が低いため、低温靭性が劣る。Steel 11 has a high C content and a low Mn content, and therefore is inferior in low temperature toughness. Steel 12 has a high amount of Si and Mn, so that the strength is good, but the low temperature toughness is poor. Since Steel 13 has a low Nb content, Steel 14 does not have Ti added, Steel 15 has a low N content, and Steel 16 has a high N content, so that the low temperature toughness is poor. Steel 17 has a high reheating temperature and thus has a low low temperature toughness. Since the steel 18 has a low reheating temperature, it is inferior in strength, adhesion between the laminated material and the base material, and corrosion resistance. Steel 19-22 is 1000
The low-temperature toughness is inferior due to the low rolling ratio above ℃.
【００４２】鋼２３は総圧下比が低いため、合わせ材と
母材の密着性が劣る。鋼２４は圧延終了温度が低いた
め、耐食性が劣る。鋼２５は圧延終了温度が高いため、
低温靭性が劣る。鋼２６は空冷時間が短いため、耐食性
が劣る。鋼２７は空冷時間が長く、水冷開始温度が低い
ため、強度、耐食性が劣る。鋼２８は冷却速度が低いた
め、強度、耐食性が劣る。鋼２９は冷却速度が高いた
め、低温靭性が劣る。鋼３０は水冷停止温度が高いた
め、強度、耐食性が劣る。Since the total reduction ratio of steel 23 is low, the adhesion between the laminated material and the base material is poor. Steel 24 has a low rolling end temperature and thus has poor corrosion resistance. Steel 25 has a high rolling end temperature, so
Inferior low temperature toughness. Steel 26 is inferior in corrosion resistance because the air-cooling time is short. Steel 27 has a long air-cooling time and a low water-cooling start temperature, and therefore is inferior in strength and corrosion resistance. Since the steel 28 has a low cooling rate, its strength and corrosion resistance are poor. Steel 29 has a low cooling rate because of its high cooling rate. Since steel 30 has a high water-cooling stop temperature, it is inferior in strength and corrosion resistance.
【００４３】[0043]
【発明の効果】本発明により、鋼管全体を溶体化処理す
ることなく、母材の強度・低温靭性、合わせ材の耐食性
がともに優れた高品質なクラッド鋼板の製造が可能とな
った。その結果、省エネルギー、省工程が可能となっ
た。また、諸特性（特に低温靭性）の向上によりパイプ
ラインの安全性が著しく向上した。According to the present invention, it is possible to manufacture a high-quality clad steel plate having excellent strength and low temperature toughness of the base material and corrosion resistance of the laminated material without subjecting the entire steel pipe to solution treatment. As a result, it has become possible to save energy and process. In addition, the safety of the pipeline has been significantly improved by improving various characteristics (especially low temperature toughness).
─────────────────────────────────────────────────────
─────────────────────────────────────────────────── ───
【手続補正書】[Procedure amendment]
【提出日】平成４年４月３０日[Submission date] April 30, 1992
【手続補正１】[Procedure Amendment 1]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】０００９[Correction target item name] 0009
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【０００９】合わせ材において優れた耐食性を得るに
は、再加熱時に合金元素を溶体化、これを高温で圧延、
適当な時間空冷してオーステナイト（γ）組織を再結晶
させ、かつ圧延後、急冷してσ相（Ｃｒ炭化物）などの
析出を抑制しなければならない。しかしながら、合わせ
材のγ組織が再結晶するような高温で圧延を行なうと、
母材の結晶粒の微細化が不十分となり、ラインパイプと
して十分な低温靭性を得ることができない。In order to obtain excellent corrosion resistance in the laminated material, the alloying elements are solution-treated at the time of reheating, and this is rolled at a high temperature,
The austenite (γ) structure must be recrystallized by air cooling for an appropriate time, and after rolling, it must be rapidly cooled to suppress precipitation of the σ phase (Cr carbide) and the like. However, when rolling at a high temperature such that the γ structure of the laminated material recrystallizes,
The refinement of the crystal grains of the base material becomes insufficient, and sufficient low temperature toughness cannot be obtained as a line pipe.
【手続補正２】[Procedure Amendment 2]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００１３[Correction target item name] 0013
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００１３】続いて１０００℃以下での圧下比が３以上
となるように圧延されなければならない。この理由は、
母材γ組織を１０００℃以下の未再結晶温度域で強圧下
することによってγ粒の伸延化、γ粒内への加工歪
の導入をはかり、γ→α変態時の核生成サイトであるγ
粒界や加工歪を増加させることでより微細な母材最終組
織を得るためである。１０００℃以下での圧下比が３未
満であると、γ粒の伸延化が不十分なためにγ→α変態
時の核生成サイトであるγ粒界の面積が少なく、同様に
核生成サイトであるγ粒内の加工歪量も少ないために、
変態後の母材最終組織は十分な微細化がなされず、優れ
た母材低温靭性は得られない。Subsequently, it must be rolled so that the rolling reduction ratio at 1000 ° C. or lower becomes 3 or higher. The reason for this is
By strongly reducing the γ structure of the base material in the unrecrystallized temperature range of 1000 ° C. or less, elongation of γ grains and introduction of processing strain into γ grains are attempted, and γ is a nucleation site during the γ → α transformation.
This is to obtain a finer final structure of the base material by increasing grain boundaries and working strain. If the reduction ratio at 1000 ° C. or less is less than 3, the elongation of the γ grains is insufficient, so that the area of the γ grain boundary which is the nucleation site during the γ → α transformation is small, and similarly at the nucleation site. Since the amount of processing strain in a certain γ grain is also small,
The final structure of the base material after transformation is not sufficiently refined, and excellent low temperature toughness of the base material cannot be obtained.
【手続補正３】[Procedure 3]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００１５[Correction target item name] 0015
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００１５】本発明では、圧延終了温度を９００℃〜１
０００℃の範囲としている。圧延終了温度が９００℃未
満であると、合わせ材のγ組織が再結晶せずに耐食性
（たとえば耐孔食性、試験状態：１０％ＦｅＣｌ3 ・６
Ｈ2 Ｏ溶液で４８時間浸漬）が著しく劣化する。合わせ
材の耐食性の観点からは圧延終了温度は高いほど好まし
い。しかし圧延終了温度が高過ぎると母材の結晶粒が微
細化せず、低温靭性の劣化を招く。このため圧延終了温
度を１０００℃以下に限定した。In the present invention, the rolling end temperature is 900 ° C to 1
The range is 000 ° C. If the rolling end temperature is lower than 900 ° C., the γ structure of the laminated material does not recrystallize and corrosion resistance (for example, pitting corrosion resistance, test state: 10% FeCl 3 .6)
48 hours immersion in H 2 O solution) significantly deteriorates. From the viewpoint of the corrosion resistance of the laminated material, the higher the rolling end temperature is, the more preferable. However, if the rolling end temperature is too high, the crystal grains of the base material do not become fine and the low temperature toughness deteriorates. Therefore, the rolling end temperature is limited to 1000 ° C or lower.
【手続補正４】[Procedure amendment 4]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００３２[Name of item to be corrected] 0032
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００３２】種々の条件でサンドイッチスラブを再加熱
・圧延・冷却してクラッド鋼板を製造し、母材の強度・
靭性（シャルピー衝撃試験）、合わせ材の耐食性（孔食
の有無で評価、試験条件：１０％ＦｅＣｌ3 ・６Ｈ2 Ｏ
溶液にＳＵＳ３１６Ｌは１５℃で４８時間、インコロイ
８２５は３０℃で４８時間浸漬）、母材と合わせ材の密
着性（超音波による探傷）を調査した。The sandwich slab is reheated, rolled and cooled under various conditions to produce a clad steel plate, and the strength of the base metal
Toughness (Charpy impact test), evaluated by the presence or absence of corrosion resistance of the cladding material (pitting, test conditions: 10% FeCl 3 · 6H 2 O
SUS316L was immersed in the solution at 15 ° C. for 48 hours and Incoloy 825 was immersed at 30 ° C. for 48 hours), and the adhesion between the base material and the laminated material (inspection by ultrasonic waves) was investigated.
【手続補正５】[Procedure Amendment 5]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００３８[Correction target item name] 0038
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００３８】[0038]
【表５】 [Table 5]
【手続補正６】[Procedure correction 6]
【補正対象書類名】明細書[Document name to be amended] Statement
【補正対象項目名】００３９[Correction target item name] 0039
【補正方法】変更[Correction method] Change
【補正内容】[Correction content]
【００３９】[0039]
【表６】 [Table 6]
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.5 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｂ２３Ｋ 103:04 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 5 Identification code Office reference number FI technical display location B23K 103: 04
Claims (2)
る合わせ材と、重量％で Ｃ ：０．０２〜０．０６、 Ｓｉ：０．５以下、 Ｍｎ：１．０〜１．８、 Ｐ ：０．０３以
下、 Ｓ ：０．００５以下 Ｎｂ：０．０８〜
０．１５、 Ｔｉ：０．００５〜０．０３、 Ａｌ：０．０５以
下、 Ｎ ：０．００２〜０．００６、 残部が鉄および不可避的不純物からなる鋼母材とを重ね
合わせて四周を溶接してスラブを組み立て、これを１１
００〜１２５０℃の温度範囲に加熱後、１０００℃を超
える温度から圧延を開始し、１０００℃以下での圧下比
を３以上、総圧下比を５以上として、圧延終了温度９０
０〜１０００℃で圧延し、３０〜２００秒間空冷した
後、７５０℃以上の温度から５〜４０℃／秒の冷却速度
で５５０℃以下の任意の温度まで冷却、その後空冷する
ことを特徴とする優れた低温靭性を有するクラッド鋼板
の製造方法。1. A laminated material made of stainless steel or a nickel alloy, and C: 0.02 to 0.06, Si: 0.5 or less, Mn: 1.0 to 1.8, P: 0. 03 or less, S: 0.005 or less Nb: 0.08 to
0.15, Ti: 0.005 to 0.03, Al: 0.05 or less, N: 0.002 to 0.006, and the remainder is iron and unavoidable impurities. Assemble the slab by welding and assemble this
After heating to a temperature range of 00 to 1250 ° C., rolling is started from a temperature exceeding 1000 ° C., a rolling reduction ratio at 1000 ° C. or lower is 3 or more, a total rolling reduction ratio is 5 or more, and a rolling finishing temperature 90
Rolling at 0 to 1000 ° C., air cooling for 30 to 200 seconds, cooling from a temperature of 750 ° C. or more to an arbitrary temperature of 550 ° C. or less at a cooling rate of 5 to 40 ° C./second, and then air cooling. A method for producing a clad steel sheet having excellent low temperature toughness.
１．０、 Ｃｒ：０．０５〜０．５、 Ｍｏ：０．０５〜
０．３、 Ｃａ：０．００１〜０．００５、 の１種または２種以上を含有することを特徴とする請求
項１記載の優れた低温靭性を有するクラッド鋼板の製造
方法。2. Ni: 0.05-1.0, Cu: 0.05-
1.0, Cr: 0.05 to 0.5, Mo: 0.05 to
0.3, Ca: 0.001-0.005, 1 type (s) or 2 or more types are contained, The manufacturing method of the clad steel plate which has the outstanding low temperature toughness of Claim 1 characterized by the above-mentioned.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4991692A JPH0825040B2 (en) | 1992-03-06 | 1992-03-06 | Method for producing clad steel sheet having excellent low temperature toughness |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4991692A JPH0825040B2 (en) | 1992-03-06 | 1992-03-06 | Method for producing clad steel sheet having excellent low temperature toughness |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05261567A true JPH05261567A (en) | 1993-10-12 |
| JPH0825040B2 JPH0825040B2 (en) | 1996-03-13 |
Family
ID=12844341
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4991692A Expired - Fee Related JPH0825040B2 (en) | 1992-03-06 | 1992-03-06 | Method for producing clad steel sheet having excellent low temperature toughness |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0825040B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100262211B1 (en) * | 1997-12-19 | 2000-07-15 | 김형국 | Method of hot roll bonding of stainless clad steel |
| WO2015059909A1 (en) | 2013-10-21 | 2015-04-30 | Ｊｆｅスチール株式会社 | Austenitic stainless steel clad steel plate and process for manufacturing same |
| KR20170063866A (en) | 2014-11-11 | 2017-06-08 | 제이에프이 스틸 가부시키가이샤 | Nickel alloy clad steel sheet and method for producing same |
| CN111918979A (en) * | 2018-03-30 | 2020-11-10 | 杰富意钢铁株式会社 | Duplex stainless steel clad steel sheet and method for manufacturing same |
| EP3778965A4 (en) * | 2018-03-30 | 2021-02-17 | JFE Steel Corporation | Two-phase stainless-clad steel sheet and method for manufacturing same |
| KR102623298B1 (en) * | 2022-12-05 | 2024-01-10 | 동국제강 주식회사 | Nickel alloy clad steel manufacturing method using thermo-mechanical control process and nickel alloy clad steel manufactured by the manufacturing method |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| EP2977478B1 (en) | 2013-05-09 | 2019-03-06 | JFE Steel Corporation | Nickel alloy clad steel having excellent grain boundary corrosion resistance properties, and method for producing same |
-
1992
- 1992-03-06 JP JP4991692A patent/JPH0825040B2/en not_active Expired - Fee Related
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100262211B1 (en) * | 1997-12-19 | 2000-07-15 | 김형국 | Method of hot roll bonding of stainless clad steel |
| WO2015059909A1 (en) | 2013-10-21 | 2015-04-30 | Ｊｆｅスチール株式会社 | Austenitic stainless steel clad steel plate and process for manufacturing same |
| CN105658831A (en) * | 2013-10-21 | 2016-06-08 | 杰富意钢铁株式会社 | Austenitic stainless steel clad steel plate and process for manufacturing same |
| EP3037567A4 (en) * | 2013-10-21 | 2016-11-16 | Jfe Steel Corp | Austenitic stainless steel clad steel plate and process for manufacturing same |
| KR20170063866A (en) | 2014-11-11 | 2017-06-08 | 제이에프이 스틸 가부시키가이샤 | Nickel alloy clad steel sheet and method for producing same |
| CN111918979A (en) * | 2018-03-30 | 2020-11-10 | 杰富意钢铁株式会社 | Duplex stainless steel clad steel sheet and method for manufacturing same |
| EP3778965A4 (en) * | 2018-03-30 | 2021-02-17 | JFE Steel Corporation | Two-phase stainless-clad steel sheet and method for manufacturing same |
| EP3778958A4 (en) * | 2018-03-30 | 2021-02-17 | JFE Steel Corporation | Two-phase stainless-clad steel sheet and method for manufacturing same |
| US11692252B2 (en) | 2018-03-30 | 2023-07-04 | Jfe Steel Corporation | Duplex stainless clad steel plate and method of producing same |
| US11891675B2 (en) | 2018-03-30 | 2024-02-06 | Jfe Steel Corporation | Duplex stainless clad steel plate and method of producing same |
| KR102623298B1 (en) * | 2022-12-05 | 2024-01-10 | 동국제강 주식회사 | Nickel alloy clad steel manufacturing method using thermo-mechanical control process and nickel alloy clad steel manufactured by the manufacturing method |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0825040B2 (en) | 1996-03-13 |
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