JPH07145452A - Tough and highly rust resistant stainless steel with excellent weldability - Google Patents
Tough and highly rust resistant stainless steel with excellent weldabilityInfo
- Publication number
- JPH07145452A JPH07145452A JP29106893A JP29106893A JPH07145452A JP H07145452 A JPH07145452 A JP H07145452A JP 29106893 A JP29106893 A JP 29106893A JP 29106893 A JP29106893 A JP 29106893A JP H07145452 A JPH07145452 A JP H07145452A
- Authority
- JP
- Japan
- Prior art keywords
- present
- toughness
- strength
- range
- rust resistance
- 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.)
- Withdrawn
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
(57)【要約】
【目的】 本発明は、９００N/mm2 以上の強度を持つ材
料において、溶接性に優れた強靭かつ高耐銹性を有する
ステンレス鋼を提供する。
【構成】 Ｃ：０．００５〜０．０５％、Ｓｉ：０．０
５〜０．８０％、Ｍｎ：０．２０〜１０．０％、Ｎｉ：
１．０〜６．５％、Ｃｕ：０．１０〜３．００％、Ｃ
ｒ：１２．０〜１５．０％、Ｍｏ：１．５〜３．０％、
Ｎ：０．００５〜０．３０％、Ｃｒ＋２．４Ｍｏ：１
７．０〜２１．５％、Ｃｒ＋１．５Ｓｉ＋１．４Ｍｏ：
１６．２〜１９．０％、Ｎｉ＋０．４Ｍｏ＋０．５Ｃｕ
＋３０Ｃ＋１８Ｎ：７．０〜１０．５％を含有し、残部
がＦｅおよび不可避的不純物から構成される。更に、Ｎ
ｂ≦０．３％、Ｖ≦０．３％、Ｔｉ≦０．３％、Ａｌ≦
０．０５％、Ｂ≦０．０１％を含有できる。
(57) [Summary] [Object] The present invention provides a stainless steel having excellent weldability, toughness, and high rust resistance in a material having a strength of 900 N / mm 2 or more. [Constitution] C: 0.005-0.05%, Si: 0.0
5 to 0.80%, Mn: 0.20 to 10.0%, Ni:
1.0 to 6.5%, Cu: 0.10 to 3.00%, C
r: 12.0 to 15.0%, Mo: 1.5 to 3.0%,
N: 0.005-0.30%, Cr + 2.4Mo: 1
7.0-21.5%, Cr + 1.5Si + 1.4Mo:
16.2-19.0%, Ni + 0.4Mo + 0.5Cu
+ 30C + 18N: 7.0 to 10.5%, with the balance being Fe and inevitable impurities. Furthermore, N
b ≦ 0.3%, V ≦ 0.3%, Ti ≦ 0.3%, Al ≦
It can contain 0.05% and B ≦ 0.01%.
Description
【０００１】[0001]
【産業上の利用分野】この発明は、９００N/mm2 以上の
引張強さを持ち、かつ溶接性と靭性に優れた高耐銹性の
素材を提供するもので、溶接施工を必要とする建設構造
物や車輌等に利用する。FIELD OF THE INVENTION The present invention provides a material having high rust resistance having a tensile strength of 900 N / mm 2 or more and excellent weldability and toughness. Used for structures and vehicles.
【０００２】[0002]
【従来の技術】従来、電車車輌用ステンレス鋼等調質圧
延により強化されている素材は、溶接部の軟化が課題
で、シーム溶接の採用が困難なためスポット溶接により
接合される。しかし、スポット溶接による施工は製品表
面に溶接による凹凸模様が発生し、美観を害する等の欠
点がある。このため、ＣＡＭＰ−ＩＳＩＪ, Vol.2(198
9),1912頁はマルテンサイト系ステンレスの採用によ
り、また、「鉄と鋼」 Vol.73(1987)， S-620頁は二相
ステンレスの採用により溶接部の高強度化を試みたこと
を開示しているが、耐銹性や靭性の点から解決には至っ
ていない現状にある。2. Description of the Related Art Conventionally, materials that have been strengthened by temper rolling, such as stainless steel for train cars, are subject to softening of welds and are difficult to adopt seam welding. However, the spot welding has a drawback in that an uneven pattern is generated on the surface of the product due to welding, which impairs the appearance. Therefore, CAMP-ISIJ, Vol.2 (198
9), page 1912 by adopting martensitic stainless steel, and "Steel and Steel" Vol.73 (1987), page S-620, by using duplex stainless steel, we tried to increase the strength of the weld. Although disclosed, it has not been solved yet in terms of rust resistance and toughness.
【０００３】[0003]
【発明が解決しようとする課題】本発明は９００N/mm2
以上の引張強さを持つ材料において、溶性部が軟化せ
ず、強靭かつ高耐銹性を有するステンレス鋼を提供する
ものである。The present invention is 900 N / mm 2
It is intended to provide a stainless steel which has toughness and high rust resistance, in which a soluble portion is not softened in a material having the above tensile strength.
【０００４】[0004]
【課題を解決するための手段】本発明は上記課題の解決
に当たり、溶接部および母材の強度、靭性と耐銹性にお
よぼす材料構成成分の影響を綿密に調査した結果、その
最適範囲が存在することを知見したことによる。In order to solve the above problems, the present invention has scrutinized the effects of the material constituents on the strength, toughness and rust resistance of the weld and the base metal, and found that the optimum range exists. It is due to the fact that it was found to do.
【０００５】即ち、本発明の溶接性に優れた強靭高耐銹
性ステンレス鋼は、重量％として、Ｃ ：０．００５〜
０．０５％、 Ｓｉ：０．０５〜０．８０％、Ｍｎ：
０．２０〜１０．０％、 Ｎｉ：１．０〜６．５％、
Ｃｕ：０．１０〜３．０％、 Ｃｒ：１２．０〜１
５．０％、Ｍｏ：１．５〜３．０％、 Ｎ ：
０．００５〜０．３０％、Ｃｒ＋２．４Ｍｏ：１７．０
〜２１．５％、Ｃｒ＋１．５Ｓｉ＋１．４Ｍｏ：１６．
２〜１９．０％、Ｎｉ＋０．４Ｍｎ＋０．５Ｃｕ＋３０
Ｃ＋１８Ｎ：７．０〜１０．５％ を含有し、残部がＦｅおよび不可避的不純物からなるこ
とを特徴とする。また、本発明は必要により、Ｎｂ≦
０．３％、Ｖ≦０．３％、Ｔｉ≦０．３％の１種または
２種以上を総量で０．３％以下、あるいは更にＡｌ≦
０．０５％、Ｂ≦０．０１％の１種または２種を含有す
ることができることを特徴とする。That is, the toughness and rust-resistant stainless steel having excellent weldability according to the present invention has a C: 0.005-0.005% by weight.
0.05%, Si: 0.05 to 0.80%, Mn:
0.20 to 10.0%, Ni: 1.0 to 6.5%,
Cu: 0.10 to 3.0%, Cr: 12.0 to 1
5.0%, Mo: 1.5 to 3.0%, N:
0.005-0.30%, Cr + 2.4Mo: 17.0
21.5%, Cr + 1.5Si + 1.4Mo: 16.
2-19.0%, Ni + 0.4Mn + 0.5Cu + 30
C + 18N: 7.0 to 10.5% is contained, and the balance is Fe and inevitable impurities. In addition, the present invention, if necessary, Nb ≦
0.3%, V ≦ 0.3%, Ti ≦ 0.3%, one or more kinds in total of 0.3% or less, or further Al ≦
One or two of 0.05% and B ≦ 0.01% can be contained.
【０００６】以下に本発明の範囲を上記に限定した理由
を述べる。Ｃは溶接部および母材部の強度を得るために
０．００５％以上添加するが、過剰の添加は靭性を害す
るため上限を０．０５％に限定した。Ｓｉは脱酸のため
に０．０５％以上添加するが、過剰の添加は溶接部およ
び母材部の靭性および耐銹性を害するため上限を０．８
％に限定した。Ｍｎは靭性を得るために０．２％以上添
加するが、過剰の添加は溶接部および母材部の靭性およ
び耐銹性を害するため上限を１０．０％に限定した。The reason why the scope of the present invention is limited to the above is described below. C is added in an amount of 0.005% or more in order to obtain the strength of the welded portion and the base metal portion, but excessive addition impairs the toughness, so the upper limit was limited to 0.05%. Si is added in an amount of 0.05% or more for deoxidation, but excessive addition impairs the toughness and rust resistance of the welded portion and the base metal portion, so the upper limit is 0.8.
Limited to%. Mn is added in an amount of 0.2% or more in order to obtain toughness, but excessive addition impairs the toughness and rust resistance of the welded portion and the base metal portion, so the upper limit was set to 10.0%.
【０００７】Ｎｉは溶接部および母材部の靭性を得るた
めに１．０％以上添加するが、過剰の添加はオーステナ
イトを生成し強度が低下するため上限を６．５％に限定
した。Ｃｕは溶接部および母材部の強度と靭性を得るた
めに０．１０％以上添加するが、過剰の添加はオーステ
ナイトを生成し強度が低下するため上限を３．０％に限
定した。Ｃｒは溶接部および母材部の強度と耐銹性を得
るため１２．０％以上添加するが、過剰の添加はフェラ
イトを生成し強度と耐銹性が低下するため上限を１５．
０％に限定した。Ni is added in an amount of 1.0% or more in order to obtain the toughness of the welded portion and the base metal portion, but excessive addition forms austenite and lowers the strength, so the upper limit was limited to 6.5%. Cu is added in an amount of 0.10% or more in order to obtain the strength and toughness of the welded portion and the base material portion, but excessive addition forms austenite and decreases the strength, so the upper limit was limited to 3.0%. Cr is added in an amount of 12.0% or more in order to obtain the strength and rust resistance of the welded portion and the base metal portion. However, an excessive addition of Cr produces ferrite to lower the strength and rust resistance, so the upper limit is 15.
Limited to 0%.
【０００８】Ｍｏは溶接部および母材部の耐銹性を得る
ため１．５％以上添加するが、過剰の添加はフェライト
を生成し靭性が低下する。またフェライトとオーステナ
イト境界に炭化物を析出し耐銹性を劣化させる。このた
め、Ｍｏの上限を３．０％に限定した。Ｎは強度を得る
ために０．００５％以上添加するが、過剰の添加は溶接
部および母材部の靭性を害するため上限を０．１０％に
限定した。Mo is added in an amount of 1.5% or more in order to obtain rust resistance of the welded portion and the base metal portion, but excessive addition produces ferrite and reduces toughness. Further, carbide is precipitated at the boundary between ferrite and austenite to deteriorate rust resistance. Therefore, the upper limit of Mo is limited to 3.0%. N is added in an amount of 0.005% or more in order to obtain strength, but excessive addition impairs the toughness of the welded portion and the base metal portion, so the upper limit was limited to 0.10%.
【０００９】Ｃｒ＋２．４Ｍｏは溶接部および母材部の
耐銹性を得るために添加する。図１はＣｒ＋２．４Ｍｏ
と継手部の耐銹性ランクの関係を示したもので本発明範
囲で優れたレイティングナンバーにあることがわかる。
即ち、Ｃｒ＋２．４Ｍｏは継手部の耐銹性を得るために
１７．０％以上添加するが、過剰の添加は溶接部および
母材部にフェライト組織を生成し強度と耐銹性を害する
ため上限を２１．５％に限定した。Cr + 2.4Mo is added to obtain rust resistance of the welded portion and the base metal portion. Figure 1 shows Cr + 2.4Mo
And the rust resistance rank of the joint portion are shown, and it is understood that the rating number is excellent in the range of the present invention.
That is, Cr + 2.4Mo is added in an amount of 17.0% or more in order to obtain rust resistance of the joint portion, but excessive addition forms a ferrite structure in the welded portion and the base metal portion and impairs strength and rust resistance. Was limited to 21.5%.
【００１０】Ｃｒ＋１．５Ｓｉ＋１．４ＭｏはＮｉ＋
０．４Ｍｎ＋０．５Ｃｕ＋３０Ｃ＋１８Ｎと関係する。
図２は前記指標と継手部の強度の関係を、また、図３は
前記指標と最も靭性の低いボンド部の靭性−延性遷移温
度の関係を示したもので、本発明範囲において両特性に
優れていることがわかる。即ち、Ｃｒ＋１．５Ｓｉ＋
１．４ＭｏおよびＮｉ＋０．４Ｍｎ＋０．５Ｃｕ＋３０
Ｃ＋１８Ｎはそれぞれ、溶接部と母材部の強度、靭性と
耐銹性を得るため１６．２％以上および７．０％以上添
加するが、過剰の添加はフェライトおよびオーステナイ
ト組織を生成し、フェライトは強度、靭性と耐銹性を、
またオーステナイトは強度を害するため上限を１９．０
％および１０．５％に限定した。Cr + 1.5Si + 1.4Mo is Ni +
Associated with 0.4Mn + 0.5Cu + 30C + 18N.
FIG. 2 shows the relationship between the index and the strength of the joint part, and FIG. 3 shows the relationship between the index and the toughness-ductility transition temperature of the bond part having the lowest toughness. Both properties are excellent in the range of the present invention. You can see that That is, Cr + 1.5Si +
1.4Mo and Ni + 0.4Mn + 0.5Cu + 30
C + 18N is added in an amount of 16.2% or more and 7.0% or more in order to obtain strength, toughness, and rust resistance of the welded portion and the base metal portion, respectively, but excessive addition forms ferrite and austenite structure, and ferrite is added. Strength, toughness and rust resistance,
Since austenite impairs strength, the upper limit is 19.0.
% And 10.5%.
【００１１】Ｎｂ，Ｖ，Ｔｉの微量添加は強度向上に効
果的なので必要に応じてその１種または２種以上を添加
しても良い。しかし、過剰の添加は、炭窒化物を形成し
溶接部および母材部の靭性を害するため、個々および総
量で上限を０．３％に限定した。特に、Ｔｉは上限を超
えて添加すると溶接ビードが乱れるようになる。Ａｌは
脱酸のため添加することができるが、過剰の添加は、溶
接性（特に溶接ビードの安定性）を害するため添加する
場合はその上限を０．０５％に限定する。Since the addition of a small amount of Nb, V, and Ti is effective for improving the strength, one or more of them may be added if necessary. However, excessive addition forms carbonitrides and impairs the toughness of the welded portion and the base metal portion. Therefore, the upper limit is limited to 0.3% individually and in the total amount. In particular, if Ti is added in excess of the upper limit, the weld bead will be disturbed. Al can be added for deoxidation, but excessive addition impairs the weldability (particularly the stability of the weld bead). Therefore, when adding Al, the upper limit is limited to 0.05%.
【００１２】Ｂは靭性を向上させる効果があり、必要に
応じ微量添加しても良い。しかし、過剰の添加は、かえ
って靭性を劣化させるばかりか耐銹性を害するので上限
を０．０１％以下に限定した。B has the effect of improving the toughness and may be added in a trace amount if necessary. However, excessive addition not only deteriorates toughness but also impairs rust resistance, so the upper limit was limited to 0.01% or less.
【００１３】[0013]
【実施例】次に、本発明の優位性を実施例と比較例を用
いて、具体的に説明する。表１〜表４に本発明例と比較
例の化学成分を、表５と表６に本発明例と比較例の母材
と継手部の強度、靭性、耐銹性および溶接ビード乱れの
有無を示す。いずれの供試材もステンレス鋼の通常の精
錬工程（電気炉または転炉溶解後真空あるいはアルゴン
／酸素脱酸処理による精錬）で溶解・精錬後連続鋳造に
より製造したスラブをそのまま５mm厚さに熱延した。そ
の後１１００℃焼入れ＋４００℃焼戻しの熱処理を行い
特性を調査した。溶接継手特性はレ型開先の５mm熱延板
を共金を用い、１５０Ａ，１８Ｖ，２４cm/minの溶接条
件でＭＩＧ溶接して評価した。なお、本発明材は冷間加
工性が良く冷延薄板に加工して使用できる。また、本発
明材は１０００〜１２００℃の範囲で焼入れ可能で、２
００〜８００℃の範囲で焼戻しできる。更に、本発明材
は溶接性が良く１２０〜３００Ａ，１２〜３０Ｖの溶接
条件で溶接して使用できる。EXAMPLES Next, the superiority of the present invention will be specifically described with reference to Examples and Comparative Examples. Tables 1 to 4 show the chemical components of the present invention example and the comparative example, and Tables 5 and 6 show the strength, toughness, rust resistance and the presence or absence of weld bead disorder of the base material and the joint portion of the present invention example and the comparative example. Show. In each test material, the slab manufactured by continuous casting after melting and refining in the usual refining process of stainless steel (refining by melting in an electric furnace or converter and vacuum or argon / oxygen deoxidation treatment) is directly heated to a thickness of 5 mm. Delayed After that, heat treatment of 1100 ° C. quenching + 400 ° C. tempering was performed to investigate the characteristics. The welded joint characteristics were evaluated by MIG welding a 5 mm hot-rolled sheet with a die groove under common welding conditions of 150 A, 18 V and 24 cm / min. The material of the present invention has good cold workability and can be used after being processed into a cold-rolled thin plate. Further, the material of the present invention can be hardened in the range of 1000 to 1200 ° C.
It can be tempered in the range of 00 to 800 ° C. Further, the material of the present invention has good weldability and can be used by welding under welding conditions of 120 to 300 A and 12 to 30 V.
【００１４】表５〜表６に示す特性の測定評価は以下の
方法によった。 （１）母材および継手強度 ＪＩＳ１３Ｂ号試験片によりＪＩＳ−Ｚ２２０１に従っ
て引張試験を行い引張強度と破断伸びを測定した。本発
明材の目標とする引張強度は９００N/mm2 以上で引張破
断伸び値は１５％以上である。 （２）靭性 熱延鋼板および継手ボンド部からＪＩＳ４号相似の衝撃
試験片を採取し脆性−延性の遷移温度を測定した。本発
明材の目標とする遷移温度は−５０℃以下である。 （３）耐銹性 ＪＩＳ−Ｚ２３７１により１００ｈ試験後面積法により
評価した。また継手部の評価はビードを中心において試
験した。本発明材の目標とするレイティングナンバーは
１０である。 （４）溶接性 溶接性は、継手部の強度と引張破断伸びおよび溶接ビー
ド乱れの有無で評価した。本発明材の目標とする継手部
強度は９００N/mm2 以上で破断伸び値は１５％以上であ
る。また、溶接後のビード形状は良好でビード乱れはな
い。The properties shown in Tables 5 to 6 were measured and evaluated by the following methods. (1) Base material and joint strength A tensile test and a breaking elongation were measured by performing a tensile test according to JIS-Z2201 using a JIS 13B test piece. The target tensile strength of the material of the present invention is 900 N / mm 2 or more, and the tensile elongation at break is 15% or more. (2) Toughness Impact test pieces similar to JIS No. 4 were sampled from the hot rolled steel sheet and the joint bond portion, and the brittle-ductile transition temperature was measured. The target transition temperature of the material of the present invention is −50 ° C. or lower. (3) Rust resistance It was evaluated by the area method after a 100-hour test according to JIS-Z2371. In addition, the evaluation of the joint portion was conducted mainly on the bead. The target rating number of the material of the present invention is 10. (4) Weldability Weldability was evaluated based on the strength of the joint, tensile elongation at break, and weld bead disorder. The target joint strength of the material of the present invention is 900 N / mm 2 or more and the breaking elongation value is 15% or more. Also, the bead shape after welding is good and there is no bead disorder.
【００１５】表１〜表６において、本発明No．１，２と
比較例No．４２，４３はＣの影響を調査したものであ
る。Ｃが本発明範囲未満のNo．４２は強度が本発明に比
較し劣っている。また、Ｃが本発明の範囲を超えるNo．
４３は引張破断伸びおよび靭性に劣っており本発明の優
位性が明らかである。本発明No．３，４と比較例No．４
４，４５はＳｉの影響を調査したものである。Ｓｉが本
発明範囲未満のNo．４４は引張破断伸びおよび靭性が本
発明に比較し劣っている。また、Ｓｉが本発明の範囲を
超えるNo．４５は靭性および耐銹性に劣っており本発明
の優位性が明らかである。本発明No．５，６と比較例N
o．４６，４７はＭｎの影響を調査したものである。Ｍ
ｎが本発明範囲未満のNo．４６は本発明に比較し靭性に
劣っている。また、Ｍｎが本発明の範囲を超えるNo．４
７は靭性と耐銹性に劣っており本発明の優位性が明らか
である。本発明No．７，８と比較例No．４８，４９はＮ
ｉの影響を調査したものである。Ｎｉが本発明範囲未満
のNo．４８は靭性が本発明に比較し劣っている。また、
Ｎｉが本発明の範囲を超えるNo．４９は強度に劣ってお
り本発明の優位性が明らかである。In Tables 1 to 6, the present invention No. 1, 2 and Comparative Example No. 42 and 43 are for investigating the influence of C. No. C is less than the range of the present invention. 42 is inferior in strength to the present invention. Further, No. in which C exceeds the range of the present invention.
No. 43 is inferior in tensile elongation at break and toughness, and the superiority of the present invention is clear. The present invention No. 3, 4 and Comparative Example No. Four
Nos. 4 and 45 are obtained by investigating the influence of Si. No. with Si less than the range of the present invention. No. 44 is inferior to the present invention in tensile elongation at break and toughness. In addition, No. in which Si exceeds the range of the present invention. No. 45 is inferior in toughness and rust resistance, and the superiority of the present invention is clear. The present invention No. 5, 6 and Comparative Example N
o. 46 and 47 are for investigating the influence of Mn. M
No. in which n is less than the range of the present invention. No. 46 is inferior in toughness as compared with the present invention. Moreover, Mn with Mn exceeding the range of the present invention. Four
No. 7 is inferior in toughness and rust resistance, and the superiority of the present invention is clear. The present invention No. 7 and 8 and Comparative Example No. 48 and 49 are N
This is an investigation of the effect of i. No. with Ni less than the range of the present invention. No. 48 is inferior in toughness to the present invention. Also,
No. in which Ni exceeds the range of the present invention. No. 49 is inferior in strength, and the superiority of the present invention is clear.
【００１６】本発明No．９，１０と比較例No．５０，５
１はＣｕの影響を調査したものである。Ｃｕが本発明範
囲未満のNo．５０は靭性が本発明に比較し劣っている。
また、Ｃｕが本発明の範囲を超えるNo．５１は強度に劣
っており本発明の優位性が明らかである。本発明No．１
１，１２と比較例No．５２，５３はＣｒの影響を調査し
たものである。Ｃｒが本発明範囲未満のNo．５２は耐銹
性が本発明に比較し劣っている。また、Ｃｒが本発明の
範囲を超えるNo．５３はフェライトが存在し、強度、靭
性と耐銹性が劣っており本発明の優位性が明らかであ
る。本発明No．１３，１４と比較例No．５４，５５はＭ
ｏの影響を調査したものである。Ｍｏが本発明範囲未満
のNo．５４は耐銹性が本発明に比較し劣っている。ま
た、Ｍｏが本発明の範囲を超えるNo．５５は靭性と耐銹
性が劣っており本発明の優位性が明らかである。本発明
No．１５，１６と比較例No．５６，５７はＮの影響を調
査したものである。Ｎが本発明範囲未満のNo．５６は強
度が本発明に比較して劣っている。また、Ｎが本発明の
範囲を超えるNo．５７は靭性が劣っており本発明の優位
性が明らかである。The present invention No. 9, 10 and Comparative Example No. Fifty, five
No. 1 is an investigation of the influence of Cu. No. with Cu less than the range of the present invention. No. 50 is inferior in toughness to the present invention.
In addition, No. in which Cu exceeds the range of the present invention. 51 is inferior in strength, and the superiority of the present invention is clear. The present invention No. 1
1, 12 and Comparative Example No. 52 and 53 are investigations of the influence of Cr. No. with Cr less than the range of the present invention. No. 52 is inferior in rust resistance to the present invention. Further, No. in which Cr exceeds the range of the present invention. No. 53 has ferrite and is inferior in strength, toughness and rust resistance, and the superiority of the present invention is clear. The present invention No. 13, 14 and Comparative Example No. 54 and 55 are M
This is a survey of the effect of o. No. in which Mo is less than the range of the present invention. No. 54 is inferior to the present invention in rust resistance. Further, No. in which Mo exceeds the range of the present invention. 55 is inferior in toughness and rust resistance, and the superiority of the present invention is clear. The present invention
No. 15, 16 and Comparative Example No. 56 and 57 are for investigating the influence of N. No. in which N is less than the range of the present invention. 56 is inferior in strength to the present invention. In addition, No. where N exceeds the range of the present invention. No. 57 is inferior in toughness, and the superiority of the present invention is clear.
【００１７】本発明No．１７，１８と比較例No．５８，
５９はＣｒ＋２．４Ｍｏの影響を調査したものである。
Ｃｒ＋２．４Ｍｏが本発明の範囲未満のNo．５８は耐銹
性が本発明に比較し劣っている。また、Ｃｒ＋２．４Ｍ
ｏが本発明の範囲を超えるNo．５９はフェライトが存在
し、靭性と耐銹性が劣っており本発明の優位性が明らか
である。本発明No．１９〜２２と比較例No．６０〜６３
はＣｒ＋１．５Ｓｉ＋１．４ＭｏおよびＮｉ＋０．４Ｍ
ｎ＋０．５Ｃｕ＋３０Ｃ＋１８Ｎの影響を調査したもの
である。Ｃｒ＋１．５Ｓｉ＋１．４Ｍｏが本発明範囲未
満のNo．６０は強度と耐銹性が本発明に比較し劣ってい
る。また、Ｃｒ＋１．５Ｓｉ＋１．４Ｍｏが本発明の範
囲を超えるNo．６１は強度、靭性と耐銹性が劣ってい
る。更に、Ｎｉ＋０．４Ｍｎ＋０．５Ｃｕ＋３０Ｃ＋１
８Ｎが本発明範囲未満のNo．６２は強度と靭性が本発明
に比較し劣っている。また、Ｎｉ＋０．２Ｍｎ＋０．５
Ｃｕ＋３０Ｃ＋１８Ｎが本発明範囲を超えるNo．６３は
強度が本発明に比較し劣っており本発明の優位性が明ら
かである。The present invention No. 17, 18 and Comparative Example No. 58,
59 is an investigation of the influence of Cr + 2.4Mo.
Cr + 2.4Mo is No. below the range of the present invention. No. 58 is inferior to the present invention in rust resistance. Also, Cr + 2.4M
No. where o exceeds the range of the present invention. No. 59 has ferrite and is inferior in toughness and rust resistance, and the superiority of the present invention is clear. The present invention No. 19 to 22 and Comparative Example No. 60-63
Is Cr + 1.5Si + 1.4Mo and Ni + 0.4M
The influence of n + 0.5Cu + 30C + 18N was investigated. Cr + 1.5Si + 1.4Mo is less than the range of the present invention. No. 60 is inferior to the present invention in strength and rust resistance. In addition, Cr + 1.5Si + 1.4Mo, which exceeds the range of the present invention, is No. No. 61 is inferior in strength, toughness and rust resistance. Furthermore, Ni + 0.4Mn + 0.5Cu + 30C + 1
No. 8N is less than the range of the present invention. No. 62 is inferior to the present invention in strength and toughness. Also, Ni + 0.2Mn + 0.5
Cu + 30C + 18N is a No. exceeding the range of the present invention. No. 63 is inferior in strength to the present invention, and the superiority of the present invention is clear.
【００１８】本発明No．２３，２４と比較例No．６４は
Ｎｂの影響を調査したものである。Ｎｂが本発明範囲を
超えるNo．６４は靭性が本発明に比較し劣っており本発
明の優位性が明らかである。本発明No．２５，２６と比
較例No．６５はＶの影響を調査したものである。Ｖが本
発明範囲を超えるNo．６５は靭性が本発明に比較し劣っ
ており本発明の優位性が明らかである。本発明No．２
７，２８と比較例No．６６はＴｉの影響を調査したもの
である。Ｔｉが本発明範囲を超えるNo．６６は靭性と溶
接ビード乱れ性が本発明に比較し劣っており本発明の優
位性が明らかである。本発明No．２９〜３３と比較例N
o．６７〜７０はＮｂ＋Ｖ＋Ｔｉの影響を調査したもの
である。Ｎｂ＋Ｖ＋Ｔｉが本発明範囲を超えるNo．６７
〜７０はいずれも靭性が本発明に比較し劣っており本発
明の優位性が明らかである。The present invention No. 23 and 24 and Comparative Example No. 64 is a result of investigating the influence of Nb. No. with Nb exceeding the range of the present invention. No. 64 is inferior in toughness to the present invention, and the superiority of the present invention is clear. The present invention No. 25, 26 and Comparative Example No. No. 65 is an investigation of the influence of V. No. V in which V exceeds the range of the present invention. No. 65 is inferior in toughness to the present invention, and the superiority of the present invention is clear. The present invention No. Two
7, 28 and Comparative Example No. 66 is an investigation of the influence of Ti. No. in which Ti exceeds the range of the present invention. No. 66 is inferior to the present invention in toughness and weld bead disorder property, and the superiority of the present invention is clear. The present invention No. 29 to 33 and Comparative Example N
o. 67 to 70 are for investigating the influence of Nb + V + Ti. No. in which Nb + V + Ti exceeds the range of the present invention. 67
No. 70 to 70 are inferior to the present invention in toughness, and the superiority of the present invention is clear.
【００１９】本発明No．３４〜３６と比較例No．７１，
７２はＡｌの影響を調査したものである。Ａｌが本発明
範囲を超えるNo．７１，７２は溶接ビード乱れ性が本発
明に比較し劣っており本発明の優位性が明らかである。
本発明No．３７〜４１と比較例No．７３〜７６はＢの影
響を調査したものである。Ｂが本発明範囲を超えるNo．
７３〜７６は、いずれも靭性と耐銹性が本発明に比較し
劣っており本発明の優位性が明らかである。The present invention No. 34 to 36 and Comparative Example No. 71,
72 is a result of investigating the influence of Al. No. in which Al exceeds the range of the present invention. Nos. 71 and 72 are inferior in weld bead turbulence to the present invention, and the superiority of the present invention is clear.
The present invention No. 37 to 41 and Comparative Example No. 73 to 76 are for investigating the influence of B. No. B exceeds the range of the present invention.
Nos. 73 to 76 are inferior to the present invention in toughness and rust resistance, and the superiority of the present invention is clear.
【００２０】[0020]
【表１】 [Table 1]
【００２１】[0021]
【表２】 [Table 2]
【００２２】[0022]
【表３】 [Table 3]
【００２３】[0023]
【表４】 [Table 4]
【００２４】[0024]
【表５】 [Table 5]
【００２５】[0025]
【表６】 [Table 6]
【００２６】[0026]
【発明の効果】上述のように、本発明によれば、溶接部
の強度低下の課題を解決し、強靭高耐銹性のステンレス
鋼を供給することが可能で産業上有効な効果がもたらさ
れる。As described above, according to the present invention, it is possible to solve the problem of the reduction in the strength of the welded portion and supply stainless steel having high toughness and high rust resistance, and to bring about an industrially effective effect. .
【図１】Ｃｒ＋２．４Ｍｏと継手部の耐銹性ランク（レ
イティングナンバー）との関係を示す図。FIG. 1 is a diagram showing a relationship between Cr + 2.4Mo and a rust resistance rank (rating number) of a joint portion.
【図２】Ｃｒ＋１．５Ｓｉ＋１．４Ｍｏと、Ｎｉ＋０．
４Ｍｎ＋０．５Ｃｕ＋３０Ｃ＋１８Ｎとの関係に基づく
強度の関係を示す図。FIG. 2 shows Cr + 1.5Si + 1.4Mo and Ni + 0.
The figure which shows the relationship of strength based on the relationship with 4Mn + 0.5Cu + 30C + 18N.
【図３】Ｃｒ＋１．５Ｓｉ＋１．４Ｍｏと、Ｎｉ＋０．
４Ｍｎ＋０．５Ｃｕ＋３０Ｃ＋１８Ｎとの関係に基づく
靭性の関係を示す図。FIG. 3 shows Cr + 1.5Si + 1.4Mo and Ni + 0.
The figure which shows the relationship of toughness based on the relationship with 4Mn + 0.5Cu + 30C + 18N.
Claims (4)
％、 Ｎｉ＋０．４Ｍｎ＋０．５Ｃｕ＋３０Ｃ＋１８Ｎ：７．
０〜１０．５％ を含有し、残部がＦｅおよび不可避的不純物からなるこ
とを特徴とする溶接性に優れた強靭高耐銹性ステンレス
鋼。1. By weight%, C: 0.005 to 0.05%, Si: 0.05 to 0.80%, Mn: 0.20 to 10.0%, Ni: 1.0 to 6. 5%, Cu: 0.10 to 3.00%, Cr: 12.0 to 15.0%, Mo: 1.5 to 3.0%, N: 0.005 to 0.30%, Cr + 2.4Mo : 17.0 to 21.5%, Cr + 1.5Si + 1.4Mo: 16.2 to 19.0
%, Ni + 0.4Mn + 0.5Cu + 30C + 18N: 7.
A tough, high rust-resistant stainless steel having excellent weldability, characterized by containing 0 to 10.5%, and the balance being Fe and unavoidable impurities.
ｂ≦０．３％、Ｖ≦０．３％、Ｔｉ≦０．３％の１種ま
たは２種以上を総量で０．３％以下を含有させたことを
特徴とする溶接性に優れた強靭高耐銹性ステンレス鋼。2. The steel according to claim 1, further comprising N in a weight percentage.
Toughness excellent in weldability, characterized by containing one or more of b ≦ 0.3%, V ≦ 0.3% and Ti ≦ 0.3% in a total amount of 0.3% or less. High rust resistant stainless steel.
Ａｌ≦０．０５重量％を含有させたことを特徴とする溶
接性に優れた強靭高耐銹性ステンレス鋼。3. The steel according to claim 1, further comprising:
A tough, high rust resistant stainless steel excellent in weldability, which is characterized by containing Al ≦ 0.05% by weight.
の鋼に、更に、Ｂ≦０．０１重量％を含有させたことを
特徴とする溶接性に優れた強靭高耐銹性ステンレス鋼。4. A tough, highly rust-resistant stainless steel having excellent weldability, which further comprises B ≦ 0.01% by weight of the steel according to claim 1, 2 or 3. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29106893A JPH07145452A (en) | 1993-11-19 | 1993-11-19 | Tough and highly rust resistant stainless steel with excellent weldability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29106893A JPH07145452A (en) | 1993-11-19 | 1993-11-19 | Tough and highly rust resistant stainless steel with excellent weldability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07145452A true JPH07145452A (en) | 1995-06-06 |
Family
ID=17764011
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP29106893A Withdrawn JPH07145452A (en) | 1993-11-19 | 1993-11-19 | Tough and highly rust resistant stainless steel with excellent weldability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07145452A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005045082A1 (en) * | 2003-11-07 | 2005-05-19 | Nippon Steel & Sumikin Stainless Steel Corporation | AUSTENITIC HIGH Mn STAINLESS STEEL EXCELLENT IN WORKABILITY |
| CN100372961C (en) * | 2003-11-07 | 2008-03-05 | 新日铁住金不锈钢株式会社 | Austenitic high Mn stainless steel with excellent workability |
| CN110312816A (en) * | 2017-02-24 | 2019-10-08 | 杰富意钢铁株式会社 | Oil well high-strength stainless steel seamless steel tube and its manufacturing method |
-
1993
- 1993-11-19 JP JP29106893A patent/JPH07145452A/en not_active Withdrawn
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2005045082A1 (en) * | 2003-11-07 | 2005-05-19 | Nippon Steel & Sumikin Stainless Steel Corporation | AUSTENITIC HIGH Mn STAINLESS STEEL EXCELLENT IN WORKABILITY |
| JP2005154890A (en) * | 2003-11-07 | 2005-06-16 | Nippon Steel & Sumikin Stainless Steel Corp | Austenitic high Mn stainless steel with excellent workability |
| CN100372961C (en) * | 2003-11-07 | 2008-03-05 | 新日铁住金不锈钢株式会社 | Austenitic high Mn stainless steel with excellent workability |
| CN110312816A (en) * | 2017-02-24 | 2019-10-08 | 杰富意钢铁株式会社 | Oil well high-strength stainless steel seamless steel tube and its manufacturing method |
| US11306369B2 (en) | 2017-02-24 | 2022-04-19 | Jfe Steel Corporation | High-strength stainless steel seamless pipe for oil country tubular goods, and method for producing same |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR100653581B1 (en) | High-strength stainless steel sheet and method for manufacturing the same | |
| JP5704721B2 (en) | High strength steel plate with excellent seam weldability | |
| JP3704306B2 (en) | Hot-dip galvanized high-strength steel sheet excellent in weldability, hole expansibility and corrosion resistance, and method for producing the same | |
| CN114423880B (en) | High-strength ultra-thick steel material having excellent low-temperature impact toughness and method for producing same | |
| US8465604B2 (en) | Ferritic stainless steel sheet having excellent corrosion resistance and method of manufacturing the same | |
| US7572407B2 (en) | Martensitic stainless steel sheet and method for making the same | |
| JP2020204091A (en) | High strength steel sheet for high heat input welding | |
| CN102782170B (en) | Low-chromium-content stainless steel with excellent corrosion resistance of weld | |
| JP3895986B2 (en) | High-strength steel plate excellent in weldability and hole expansibility and method for producing the same | |
| JPH0953155A (en) | Fe-Cr alloy with excellent ridging resistance and surface properties | |
| JP4495064B2 (en) | Steel sheet for hot press | |
| JP4022019B2 (en) | High-strength cold-rolled steel sheet with excellent formability after welding and difficult to soften weld heat-affected zone | |
| JP4457492B2 (en) | Stainless steel with excellent workability and weldability | |
| JPH07145452A (en) | Tough and highly rust resistant stainless steel with excellent weldability | |
| EP1378580A1 (en) | Structural Fe-Cr steel sheet, manufacturing method thereof, and structural shaped steel | |
| EP1026274A1 (en) | High-strength steel plate reduced in softening in weld heat-affected zone | |
| JP4192576B2 (en) | Martensitic stainless steel sheet | |
| JP4273457B2 (en) | Structural stainless steel plate with excellent hole expansion workability | |
| JP3705161B2 (en) | High tensile steel plate | |
| US20080213121A1 (en) | Steel For Submarine Hulls With Improved Weldability | |
| JP3943754B2 (en) | High-strength cold-rolled steel sheet and high-strength surface-treated steel sheet that have excellent fatigue properties of the base metal and formability after welding, and are difficult to soften the heat affected zone. | |
| JPH07113145A (en) | Tough and rust resistant stainless steel with excellent weldability | |
| JP3975882B2 (en) | High corrosion resistance low strength stainless steel with excellent workability and toughness of welds and its welded joints | |
| JP3491625B2 (en) | Fe-Cr alloy with excellent initial rust resistance, workability and weldability | |
| JP3933020B2 (en) | Stainless steel with excellent fatigue characteristics and toughness of fillet welded joints when forming fillet welded joints |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20010130 |