JP3313440B2 - High corrosion resistance high strength clad steel and method for producing the same - Google Patents
High corrosion resistance high strength clad steel and method for producing the sameInfo
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- JP3313440B2 JP3313440B2 JP04878993A JP4878993A JP3313440B2 JP 3313440 B2 JP3313440 B2 JP 3313440B2 JP 04878993 A JP04878993 A JP 04878993A JP 4878993 A JP4878993 A JP 4878993A JP 3313440 B2 JP3313440 B2 JP 3313440B2
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Description
【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION
【０００１】[0001]
【産業上の利用分野】この発明は、高い耐食性と強度が
要求される用途に使用される高耐食性高強度クラッド鋼
およびそ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 relates to a high-corrosion-resistant high-strength clad steel used for applications requiring high corrosion resistance and strength, and a method for producing the same.
【０００２】[0002]
【従来の技術】従来、石油関連設備や化学工業用プラン
ト器機などに使用される材料は、特に高い耐食性が要求
されるため、Ｃ−Ｍn 鋼やＣ−Ｍn−Ｓi 鋼などの溶接
構造用鋼（母材）に、耐食性が非常に優れたＪＩＳ Ｇ
４９０１ ＮＣＦ８２５ Ｆe 基合金（合せ材）をクラッ
ドしたクラッド鋼が使用されている。上記したクラッド
鋼では、耐食性を確保するために合せ材に対して、高温
での溶体化処理が必要であり、圧延後にクラッド鋼全体
を高温に加熱して焼準し処理を行っている。2. Description of the Related Art Conventionally, materials used for petroleum-related equipment and plant equipment for the chemical industry are required to have particularly high corrosion resistance, so that welding structural steels such as C-Mn steel and C-Mn-Si steel are required. (Base material), JIS G with very excellent corrosion resistance
Clad steel clad with 4901 NCF825 Fe-based alloy (combined material) is used. In the above-mentioned clad steel, a solution treatment at a high temperature is necessary for the composite material in order to secure corrosion resistance, and after the rolling, the entire clad steel is heated to a high temperature and normalized.
【０００３】[0003]
【発明が解決しようとする課題】しかし、例えば近年の
石油・天然ガス事業では、産出物のサワー化等により腐
食性が増す傾向にあり、耐食性の高い合せ材を使用した
クラッド鋼の適用が求められているが、その中でも特に
寒冷地のラインパイプ用材として前述の母材及び製法に
よって製造されたクラッド鋼を使用するには、それに要
求される強度、靱性が非常に高いレベルにあることか
ら、溶接性を含めたそれら全てを満足することは困難で
ある。すなわち、母材の高強度化を行うと溶接性及び靱
性が低下し、高靱性化を行うと引張強度の低下などが起
こる。溶接性と強度、靱性を同時に確保し得る方法とし
て制御圧延制御冷却法（ＴＭＣＰプロセス）があるが、
この方法により製造されたクラッド鋼ではその製法上の
理由から熱間加工を行うことが難しく、したがって例え
ばラインパイプ部材のうち、特にエルボ管、ティー字
管、ベンド管といった強加工を伴う部材を製造すること
は困難である。また、ＴＭＣＰ管の溶接部は、熱影響部
が軟化し易く、溶接部近傍の強度が要求を満足できない
といった問題を起こす可能性があった。この発明は、上
記事情を背景としてなされたものであり、合せ材の耐食
性を十分に得るとともに、母材の強度低下を防止して、
耐食性および強度、靱性に優れ、熱間加工等の再加熱を
要する部材の製造にも適したクラッド鋼およびその製造
方法を提供することを目的とする。However, in the recent petroleum and natural gas business, for example, the corrosiveness tends to increase due to the sourcing of products, and the application of clad steel using a highly corrosion-resistant composite material is required. However, among them, in order to use clad steel manufactured by the above-described base metal and the manufacturing method particularly as a material for line pipes in cold regions, since the strength and toughness required for it are at a very high level, It is difficult to satisfy all of them including weldability. That is, when the strength of the base material is increased, the weldability and toughness are reduced, and when the toughness is increased, the tensile strength is reduced. As a method that can simultaneously secure weldability, strength, and toughness, there is a controlled rolling control cooling method (TMCP process).
With the clad steel manufactured by this method, it is difficult to perform hot working for the reason of the manufacturing method. Therefore, for example, among the line pipe members, particularly, members that require strong working such as elbow pipes, tee pipes, and bend pipes are manufactured. It is difficult to do. Further, in the welded portion of the TMCP pipe, the heat-affected zone is likely to be softened, and there is a possibility that the strength near the welded portion cannot satisfy the requirement. The present invention has been made in view of the above circumstances, and while sufficiently obtaining the corrosion resistance of the composite material, preventing a decrease in the strength of the base material,
An object of the present invention is to provide a clad steel excellent in corrosion resistance, strength, and toughness and suitable for manufacturing a member requiring reheating such as hot working, and a method for manufacturing the same.
【０００４】[0004]
【課題を解決するための手段】上記課題を解決するた
め、本願発明の高耐食性高強度クラッド鋼の製造方法
は、母材組成が、重量％で、Ｃ：０．０５〜０．１２
％、Ｓi ：０．５％以下、Ｍn ：１〜１．８％、Ｎb ：
０．０６％以下、Ｍo ：０．２５％以下、Ｖ：０．０６
％以下、Ａl ：０．０１〜０．０６％を含有し、残部が
Ｆe および不可避不純物からなり、合せ材組成が、Ｃ：
０．０５％以下、Ｓi ：０．５％以下、Ｍn ：１％以
下、Ｃr ：１９．５〜２３．５％、Ｍo ：２．５〜３．
５％、Ａl ：０．２％以下、Ｔi ：０．６〜１．２％、
Ｃu ：１．５〜３％、Ｎi ：３８〜４６％を含有し、残
部がＦe および不可避不純物からなるクラッド鋼を９０
０〜１０３０℃に加熱した後、焼入し、その後、５００
〜６３０℃の焼戻しを行うことを特徴とする。 Means for Solving the Problems To solve the above problems,
The high corrosion resistance and high strength clad steel of the present inventionManufacturing method
Means that the composition of the base material is% by weight, C: 0.05 to 0.12
%, Si: 0.5% or less, Mn: 1 to 1.8%, Nb:
0.06% or less, Mo: 0.25% or less, V: 0.06
% Or less, Al: 0.01 to 0.06%, with the balance being
Fe and unavoidable impurities, and the composition of the composite material is C:
0.05% or less, Si: 0.5% or less, Mn: 1% or less
Below, Cr: 19.5-23.5%, Mo: 2.5-3.
5%, Al: 0.2% or less, Ti: 0.6-1.2%,
Cu: 1.5 to 3%, Ni: 38 to 46%,
The part is made of Fe and unavoidable impurities.90 clad steel
After heating to 0 to 1030 ° C., quenching, then 500
It is characterized by performing tempering at 〜630 ° C.
【０００５】なお、母材の組成には、上記元素の他にも
Ｐ、Ｓ、Ｎi、Ｃr、Ｃu などの不純物が含まれるが、こ
れら不純物は、製鋼上不可避的に含有されるものであ
り、極力低減するのが望ましい。[0005] The Contact, the composition of the base material, P in addition to the above elements, S, Ni, Cr, but containing impurities such as Cu, these impurities are intended to be contained in steel on unavoidably Yes, it is desirable to reduce as much as possible.
【０００６】[0006]
【作用】すなわち、本願発明のクラッド鋼によれば、合
せ材の溶体化処理温度に合わせてクラッド鋼を加熱して
も、母材では結晶粒の粗大化による軟化などは生じな
い。そして、この温度は、母材の焼入れ可能温度にも相
当しており、加熱後急冷することにより、母材が焼入れ
されて強度が向上する。さらに、このクラッド鋼を、母
材に合わせて焼戻しすることにより、合せ材の鋭敏化温
度域を外れた温度で焼戻しを行うことができ、合せ材の
耐食性を損なうことなく母材の靱性を向上させることが
できる。In other words, according to the clad steel of the present invention, even if the clad steel is heated in accordance with the solution treatment temperature of the composite material, the base material does not soften due to the coarsening of the crystal grains. This temperature also corresponds to the temperature at which the base material can be hardened. By rapidly cooling after heating, the base material is hardened and the strength is improved. Furthermore, by tempering this clad steel in accordance with the base metal, it can be tempered at a temperature outside the sensitized temperature range of the base material, improving the toughness of the base material without impairing the corrosion resistance of the base material. Can be done.
【０００７】さらに、設定温度範囲で加熱することによ
り、合せ材は良好に溶体化処理され、優れた耐食性が発
揮される。一方、母材では、結晶粒の粗大化が生ずるこ
となく、微細なオーステナイト組織となる。これを急冷
（例えば水冷以上の冷却速度）することにより、母材は
フェライト＋ベイナイト又はベイナイト＋マルテンサイ
トの混合組織となり、高い強度が得られる。さらに、焼
戻しにおける設定温度範囲は、合せ材の鋭敏化温度域
（６５０〜７６０℃）を外れており、合せ材の耐食性を
損なうことなく焼戻しを行うことができる。以下に、本
願発明における母材および合せ材の成分限定理由を述べ
る。Further , by heating in the set temperature range, the composite material is subjected to a good solution treatment and excellent corrosion resistance is exhibited. On the other hand, the base material has a fine austenite structure without coarsening of crystal grains. By rapidly cooling this (for example, a cooling rate higher than water cooling), the base material becomes a mixed structure of ferrite + bainite or bainite + martensite, and high strength can be obtained. Further, the set temperature range in the tempering is out of the sensitizing temperature range (650 to 760 ° C.) of the composite material, so that the tempering can be performed without impairing the corrosion resistance of the composite material. The reasons for limiting the components of the base material and the composite in the present invention are described below.
【０００８】（母材）Ｃ：０．０５〜０．１２％ Ｃは、必要な引張強さを確保するために添加する。その
含有量が０．０５％未満では、必要な強度が確保でき
ず、また、０．１２％を超えると、溶接性および靭性を
害するので、上記範囲内とした。 Ｓi ：０．５％以下 Ｓi は脱酸剤として添加されるが、０．５％を越えて含
有すると、靭性の低下が著しいため上限を定めた。( Base material) C: 0.05 to 0.12% C is added in order to secure necessary tensile strength. If the content is less than 0.05 %, the required strength cannot be secured, and if it exceeds 0.12%, the weldability and toughness are impaired. Si: 0.5% or less Si is added as a deoxidizing agent, but if it exceeds 0.5%, the toughness is significantly reduced, so the upper limit was set.
【０００９】Ｍn ：１〜１．８％ Ｍn は、Ｃr に代わり引張強さを向上させ、溶接性を確
保するという観点から１％以上含有させる必要がある。
ただし、１．８％を超えると靱性を害するので上記範囲
内とした。Ｎb ：０．０６％以下 Ｎb は焼戻し後の軟化の抑制とオーステナイト化状態で
の結晶粒の微細化による靱性の向上を目的に添加する。
但し、０．０６％を越えて含有させると、溶接熱影響部
の脆化を招くので０．０６％を上限とした。 Mn: 1 to 1.8% Mn must be contained in an amount of 1% or more from the viewpoint of improving tensile strength and securing weldability instead of Cr.
However, if the content exceeds 1.8%, the toughness is impaired. Nb: 0.06% or less Nb is added for the purpose of suppressing softening after tempering and improving toughness by refining crystal grains in an austenitized state.
However, if the content exceeds 0.06%, embrittlement of the weld heat affected zone is caused, so the upper limit was made 0.06%.
【００１０】Ｍo ：０．２５％以下 Ｍo は、本発明鋼において焼入れ性を向上させ、組織の
ベイナイト化あるいはマルテンサイト化に有効に作用
し、強度を向上させる。ただし、その含有量が０．２５
％を越えると、靱性の低下を招き、また溶接性を損なう
ことから上限を０．２５％に定めた。Ｖ：０．０６％以下 Ｖは、焼戻し後の所望耐力の維持向上を目的に添加す
る。但し、０．０６％を超えて含有させると、衝撃値を
低下させるので、上限を０．０６％に定めた。 Mo: 0.25% or less Mo improves the hardenability of the steel of the present invention, effectively acts on the formation of bainite or martensite in the structure, and improves the strength. However, the content is 0.25
%, The toughness is reduced and the weldability is impaired, so the upper limit was set to 0.25%. V: 0.06% or less V is added for the purpose of maintaining and improving the desired yield strength after tempering. However, if the content exceeds 0.06%, the impact value decreases, so the upper limit is set to 0.06%.
【００１１】Ａl ：０．０１〜０．０６％ Ａl は通常脱酸剤として添加され、一部は鋼中にＡlＮ
として析出し、オーステナイト結晶粒を細粒化する作用
があるが、細粒化に十分な効果を得るためには０．０１
％以上含有させる必要がある。一方、０．０６％を超え
ると熱間加工性を害するので、上限を０．０６％に定め
た。 （合せ材）合せ材は、ＪＩＳ Ｇ４９０１に、ＮＣＦ８
２５として規定されている公知のＦe 基合金であるの
で、成分限定の理由は省略する。 Al: 0.01 to 0.06% Al is usually added as a deoxidizer, and part of AlN is contained in steel.
Has the effect of refining austenite crystal grains, but in order to obtain a sufficient effect for refining, 0.01
% Or more. On the other hand, if it exceeds 0.06%, the hot workability is impaired, so the upper limit was set to 0.06%. (Material) The mate material is NCF8 according to JIS G4901.
Since it is a known Fe-based alloy specified as 25, the reason for limiting the components is omitted.
【００１２】次に、本願発明の製造方法で、焼入の加熱
温度等を限定した理由を以下に述べる。焼入加熱温度：９００〜１０３０℃ 加熱温度は合せ材の析出物が十分に固溶される温度域で
あり、また、母材の焼入可能温度に相当するものであ
り、これらの作用を得るための下限として９００℃を採
用した。一方、上限の１０３０℃を越えると、母材の結
晶粒が粗大化して衝撃値が低下するため上記範囲とし
た。焼入冷却速度 加熱後の冷却は、要求される機械的性質や材料の質量な
どにより適宜選定する。通常は、水冷で行われる。その
後は、靱性の向上を目的として焼戻しを行う。Next, the reason why the heating temperature for quenching is limited in the manufacturing method of the present invention will be described below. Quenching heating temperature: 900 to 1030 ° C. The heating temperature is a temperature range in which the precipitates of the composite material are sufficiently dissolved, and corresponds to the quenching temperature of the base material, and these effects are obtained. 900 ° C. was adopted as the lower limit for this. On the other hand, if the temperature exceeds the upper limit of 1030 ° C., the crystal grains of the base material become coarse and the impact value decreases, so that the above range was set. Quenching Cooling rate Cooling after heating is appropriately selected depending on required mechanical properties, mass of the material, and the like. Usually, it is performed by water cooling. After that, tempering is performed for the purpose of improving toughness.
【００１３】焼戻し温度：５００〜６３０℃ 焼戻し温度は、母材の靱性の回復のための下限として５
００℃を採用した。一方、合わ材の耐食性を損なわない
ための上限の温度として６３０℃を採用した。この温度
範囲は、合せ材の鋭敏化温度域を外れており、合せ材の
優れた耐食性が損なわれることはない。 Tempering temperature: 500 to 630 ° C. The tempering temperature is 5 as a lower limit for recovering the toughness of the base material.
00 ° C was employed. On the other hand, 630 ° C. was adopted as the upper limit temperature so as not to impair the corrosion resistance of the composite material. This temperature range is outside the sensitizing temperature range of the composite material, and the excellent corrosion resistance of the composite material is not impaired.
【００１４】[0014]
【実施例】以下に、本発明の実施例を、従来材法及び従
来法と比較して説明する。表１に示す組成を有する母材
用の供試鋼（本発明の母材及び比較材）５０ｋｇを高周
波真空溶解炉を用いて溶解した。さらに、合せ材とし
て、表２の組成を有するＮＣＦ８２５Ｆe 基合金を用意
し、前記母材とこの合せ材とを重ね合わせ、１１７０℃
に均熱後、熱間圧延を行い、２５ｍｍ厚（合せ材２．５
ｍｍ＋母材２２．５ｍｍ）のクラッド鋼供試材に圧延し
た。なお、表中の供試材Ｎｏ．は、使用母材Ｎｏ．と一
致している。EXAMPLES Examples of the present invention will be described below in comparison with a conventional material method and a conventional method. 50 kg of a base material test steel having the composition shown in Table 1 (base material of the present invention and comparative material) was melted using a high-frequency vacuum melting furnace. Further, an NCF825Fe-based alloy having a composition shown in Table 2 was prepared as a bonding material.
After hot soaking, hot rolling was performed to obtain a 25 mm thick
mm + base material 22.5 mm). The test material No. in the table was used. Is used base material No. Matches.
【００１５】次いで、各クラッド鋼供試材を、９４０℃
に加熱して溶体化処理を行った後、Ｎｏ．１，２，３に
ついて水焼入れし、その後、６００℃×１時間の焼戻し
を行った。また、Ｎｏ．４，５は、９４０℃に加熱した
後、空中放冷（焼準し）した。得られた各供試材につい
て、合せ材について腐食試験、母材について機械的性質
を評価する試験を行い、その結果を表３に示した。 な
お、衝撃性質は、２ｍｍＶノッチを用いたシャルピー衝
撃試験で評価し、衝撃吸収エネルギーは、−３０℃にお
ける値で示した。特に寒冷地のラインパイプ等の低温用
途に用いる場合は、シャルピー衝撃試験で得られたＦＡ
ＴＴが−９０℃以下であることが一つの目安となってい
るので、ここではＦＡＴＴで評価することとした。Next, each clad steel test material was heated at 940 ° C.
After performing the solution treatment by heating to Water quenching was performed for 1, 2, and 3, and then tempering was performed at 600 ° C for 1 hour. In addition, No. Samples 4 and 5 were heated to 940 ° C. and then allowed to cool in the air (normalized). For each of the obtained test materials, a corrosion test was performed on the composite material, and a test for evaluating the mechanical properties of the base material was performed. The results are shown in Table 3. The impact properties were evaluated by a Charpy impact test using a 2 mm V notch, and the impact absorption energy was indicated by a value at −30 ° C. In particular, when used in low-temperature applications such as line pipes in cold regions, the FA obtained by the Charpy impact test
One guideline is that TT is −90 ° C. or less, and therefore, FATT was used here for evaluation.
【００１６】表３から明らかなように、発明材を用い発
明法の熱処理を施したものは、優れた耐食性を有すると
ともに、高い引張強度と靱性が得られる。これに対し、
発明法であるが、比較材を用いたＮｏ．３は、合せ材の
耐食性と母材の引張強度は良好であるものの、強度確保
のためにＣ量が高いことから、靱性が劣っている。ま
た、比較法によって熱処理を行ったＮｏ．４，５は、耐
食性は良好であるものの引張性質と靱性が劣っている。As is apparent from Table 3, the material subjected to the heat treatment of the invention method using the invention material has excellent corrosion resistance and high tensile strength and toughness. In contrast,
The method of the invention is the same as that of the method of Comparative Example. In No. 3, although the corrosion resistance of the composite material and the tensile strength of the base material were good, the toughness was inferior because the C content was high to secure the strength. In addition, the heat treatment was performed by the comparative method. Nos. 4 and 5 have good corrosion resistance but poor tensile properties and toughness.
【００１７】[0017]
【表１】 [Table 1]
【００１８】[0018]
【表２】 [Table 2]
【００１９】[0019]
【表３】 [Table 3]
【００２０】[0020]
【発明の効果】以上説明したように、本願発明によれ
ば、母材組成が、重量％で、Ｃ：０．０５〜０．１２
％、Ｓi ：０．５％以下、Ｍn ：１〜１．８％、Ｎb ：
０．０６％以下、Ｍo ：０．２５％以下、Ｖ：０．０６
％以下、Ａl ：０．０１〜０．０６％を含有し、残部が
Ｆe および不可避不純物からなり、合せ材組成が、Ｃ：
０．０５％以下、Ｓi ：０．５％以下、Ｍn ：１％以
下、Ｃr ：１９．５〜２３．５％、Ｍo ：２．５〜３．
５％、Ａl ：０．２％以下、Ｔi ：０．６〜１．２％、
Ｃu ：１．５〜３％、Ｎi ：３８〜４６％を含有し、残
部がＦe および不可避不純物からなり、上記クラッド鋼
を９００〜１０３０℃に加熱した後、焼入し、その後、
５００〜６３０℃の焼戻しを行うので、得られたクラッ
ド鋼は、合せ材の優れた耐食性が十分に発揮され、さら
に、母材の結晶粒の粗大化が阻止されて高い強度と優れ
た靭性が得られる効果がある。As described in the foregoing, according to the present onset bright, the matrix composition, in weight%, C: 0.05 to 0.12
%, Si: 0.5% or less, Mn: 1 to 1.8%, Nb:
0.06% or less, Mo: 0.25% or less, V: 0.06
% Or less, Al: 0.01 to 0.06%, the balance being Fe and unavoidable impurities,
0.05% or less, Si: 0.5% or less, Mn: 1% or less, Cr: 19.5-23.5%, Mo: 2.5-3.
5%, Al: 0.2% or less, Ti: 0.6-1.2%,
Cu: 1.5 to 3% Ni: contained 38 to 46%, the balance being Fe and unavoidable impurities, was heated on SL clad steel from 900 to 1,030 ° C., and ShoIri, then,
Since the tempering is performed at 500 to 630 ° C., the obtained clad steel sufficiently exhibits the excellent corrosion resistance of the composite material, and further, the coarsening of the crystal grains of the base material is prevented, and the high strength and excellent toughness are obtained. There is an effect that can be obtained.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 - 38/60 ──────────────────────────────────────────────────続 き Continued on front page (58) Field surveyed (Int. Cl. 7 , DB name) C22C 38/00-38/60
Claims (1)
０．１２％、Ｓi ：０．５％以下、Ｍn ：１〜１．８
％、Ｎb ：０．０６％以下、Ｍo ：０．２５％以下、
Ｖ：０．０６％以下、Ａl ：０．０１〜０．０６％を含
有し、残部がＦe および不可避不純物からなり、合せ材
組成が、Ｃ：０．０５％以下、Ｓi ：０．５％以下、Ｍ
n ：１％以下、Ｃr ：１９．５〜２３．５％、Ｍo ：
２．５〜３．５％、Ａl ：０．２％以下、Ｔi ：０．６
〜１．２％、Ｃu ：１．５〜３％、Ｎi ：３８〜４６％
を含有し、残部がＦe および不可避不純物からなるクラ
ッド鋼を９００〜１０３０℃に加熱した後、焼入し、そ
の後、５００〜６３０℃の焼戻しを行うことを特徴とす
る高耐食性高強度クラッド鋼の製造方法。1. The composition of a base material is C: 0.05-% by weight.
0.12%, Si: 0.5% or less, Mn: 1 to 1.8
%, Nb: 0.06% or less, Mo: 0.25% or less,
V: 0.06% or less, Al: 0.01 to 0.06%, the balance is composed of Fe and unavoidable impurities, and the composition of the composite material is C: 0.05% or less, Si: 0.5%. Hereinafter, M
n: 1% or less, Cr: 19.5 to 23.5%, Mo:
2.5 to 3.5%, Al: 0.2% or less, Ti: 0.6
1.2%, Cu: 1.5-3%, Ni: 38-46%
Of a high-corrosion-resistant high-strength clad steel characterized in that the clad steel containing Fe and the balance consisting of Fe and unavoidable impurities is heated to 900 to 1030 ° C., quenched, and then tempered at 500 to 630 ° C. Production method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04878993A JP3313440B2 (en) | 1993-02-16 | 1993-02-16 | High corrosion resistance high strength clad steel and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04878993A JP3313440B2 (en) | 1993-02-16 | 1993-02-16 | High corrosion resistance high strength clad steel and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06240407A JPH06240407A (en) | 1994-08-30 |
| JP3313440B2 true JP3313440B2 (en) | 2002-08-12 |
Family
ID=12813006
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP04878993A Expired - Lifetime JP3313440B2 (en) | 1993-02-16 | 1993-02-16 | High corrosion resistance high strength clad steel and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3313440B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US11344968B2 (en) | 2016-08-12 | 2022-05-31 | Voestalpine Grobblech Gmbh | Method for producing roll-bonded metal sheets |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1347069B1 (en) * | 2000-12-20 | 2007-11-07 | Nippon Steel Corporation | High-strength spring steel and spring steel wire |
| US7396422B2 (en) | 2002-11-05 | 2008-07-08 | Kent Engineering | Rolling bearing, material for rolling bearing, and equipment having rotating part using the rolling bearing |
| CN108149139A (en) * | 2017-12-28 | 2018-06-12 | 安徽应流集团霍山铸造有限公司 | A kind of preparation method of New-type cast steel material microalloying |
-
1993
- 1993-02-16 JP JP04878993A patent/JP3313440B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US11344968B2 (en) | 2016-08-12 | 2022-05-31 | Voestalpine Grobblech Gmbh | Method for producing roll-bonded metal sheets |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH06240407A (en) | 1994-08-30 |
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