JP2003253403A - Martensitic stainless steel sheet - Google Patents
Martensitic stainless steel sheetInfo
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- JP2003253403A JP2003253403A JP2002347132A JP2002347132A JP2003253403A JP 2003253403 A JP2003253403 A JP 2003253403A JP 2002347132 A JP2002347132 A JP 2002347132A JP 2002347132 A JP2002347132 A JP 2002347132A JP 2003253403 A JP2003253403 A JP 2003253403A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、耐食性、溶接部靱
性に優れるばかりでなく、加工性にも優れるマルテンサ
イト系ステンレス鋼およびその製造方法に関するもので
あり、特に、鉄道車両や自動車、バスなどの車両の、曲
げ加工を施して形成される構造部材に用いるマルテンサ
イト系ステンレス鋼板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 martensitic stainless steel which is excellent not only in corrosion resistance and toughness of a welded portion but also in workability, and a method for producing the same, and particularly to rail cars, automobiles, buses and the like. The present invention relates to a martensitic stainless steel plate used for a structural member formed by bending of the vehicle and a manufacturing method thereof.
【０００２】[0002]
【従来の技術】従来、腐食による肉厚減に起因する強度
低下防止あるいは美観の観点から、耐食性が必要とされ
る車両構造部材、例えば、鉄道車両の構造部材として
は、耐食性に優れたSUS301L やSUS304などのオーステナ
イト系ステンレス鋼板が使用されている。オーステナイ
ト系ステンレス鋼板を車両構造部材として用いる場合、
熱延鋼板あるいは冷延鋼板の焼鈍仕上げ材では、強度が
不十分であるため、オーステナイト系ステンレス鋼板に
特有の高い加工硬化能を利用した調質圧延により強度向
上を図っている。2. Description of the Related Art Conventionally, from the viewpoint of prevention of strength reduction due to thickness reduction due to corrosion or aesthetics, as a vehicle structural member that requires corrosion resistance, for example, as a structural member of a railway vehicle, SUS301L or the like having excellent corrosion resistance is used. Austenitic stainless steel sheets such as SUS304 are used. When using austenitic stainless steel sheet as a vehicle structural member,
Since the strength of annealed finished materials of hot-rolled steel sheets or cold-rolled steel sheets is insufficient, the strength is improved by temper rolling utilizing the high work hardening ability unique to austenitic stainless steel sheets.
【０００３】しかしながら、オーステナイト系ステンレ
ス鋼板を車両構造部材に加工し、構造部材を溶接した場
合、溶接による入熱を受けた溶接部では、調質圧延で導
入した歪みが回復し、溶接部が軟化してしまい、溶接部
の強度および疲労特性が低下する問題が生じた。またフ
ェライト系ステンレス鋼では、溶接部で結晶粒が粗大化
し、溶接部靱性が極度に低下する問題があった。この欠
点を改善するため、溶接部の軟化が起こらず、かつ溶接
部靱性の優れたマルテンサイト系ステンレス鋼板を車両
構造部材に利用しようということが提案されている（例
えば、特許文献１参照）。However, when an austenitic stainless steel plate is processed into a vehicle structural member and the structural member is welded, the strain introduced by temper rolling is recovered in the welded part where the heat input by the welding is recovered, and the welded part is softened. As a result, there arises a problem that the strength and fatigue characteristics of the welded part are deteriorated. Further, in the ferritic stainless steel, there is a problem that the crystal grains are coarsened in the welded portion and the weld toughness is extremely lowered. In order to improve this drawback, it has been proposed to use a martensitic stainless steel sheet that does not soften the welded portion and has excellent welded portion toughness as a vehicle structural member (see, for example, Patent Document 1).
【０００４】しかしながら、特許文献１に記載されてい
るマルテンサイト系ステンレス鋼は、900MPa以上の高い
強度を得ることに重点をおいていたため、Mn、Ni、Mo、
Ｎなどの含有量が高く、曲げ加工を行った場合、曲げ加
工された部材の曲げの外側部分に割れが発生してしま
い、鉄道車両の構造部材や自動車、バスなどの車両の構
造部材に用いることができないという問題点があった。However, since the martensitic stainless steel described in Patent Document 1 focuses on obtaining a high strength of 900 MPa or more, Mn, Ni, Mo,
When the content of N and the like is high and bending is performed, cracks occur in the outer portion of the bending of the bent member, and it is used as a structural member of a railway vehicle or a structural member of a vehicle such as an automobile or a bus. There was a problem that I could not do it.
【０００５】このように、マルテンサイト系ステンレス
鋼板については、耐食性および溶接熱影響部での靱性に
加え、高強度を得る検討が行われているが、車両構造部
材に加工して用いることを考慮し、耐食性および溶接熱
影響部での靱性に加え、加工性、特に曲げ加工性に優れ
るマルテンサイト系ステンレス鋼については、これまで
見当らなかったのである。As described above, with respect to the martensitic stainless steel sheet, it has been studied to obtain high strength in addition to corrosion resistance and toughness in the heat-affected zone of welding, but it is considered to be used as a structural member of vehicle. However, martensitic stainless steel, which is excellent in workability, particularly bending workability, in addition to corrosion resistance and toughness in the heat-affected zone of welding, has not been found so far.
【０００６】[0006]
【特許文献１】特開平7-145452号公報[Patent Document 1] JP-A-7-145452
【０００７】[0007]
【発明が解決しようとする課題】そこで、本発明の目的
は、前記の問題を解決し、耐食性、溶接部の靱性に加
え、加工性に優れる高強度マルテンサイト系ステンレス
鋼板およびその製造方法を提供することにある。SUMMARY OF THE INVENTION Therefore, an object of the present invention is to solve the above problems and provide a high-strength martensitic stainless steel sheet excellent in workability in addition to corrosion resistance and toughness of a welded portion, and a method for producing the same. To do.
【０００８】[0008]
【課題を解決するための手段】本発明に係るマルテンサ
イト系ステンレス鋼板は、鋼板の組成または溶鋼の組成
が質量％で、Ｃ：0.02％未満、Si：1.0 ％以下、Mn：1.
5 ％未満、Ｐ：0.04％以下、Ｓ：0.01％以下、Al：0.1
％以下、Ni：1.5 ％以上、4.0 ％未満、Cr：11％以上、
15％未満、Mo：0.5 ％以上、2.0 ％未満、Ｎ：0.02％未
満、を含有し、15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×
〔Ni〕≦20.0％と、〔Ｃ〕＋〔Ｎ〕＜0.030 ％と、〔N
i〕＋0.5 ×（〔Mn〕＋〔Mo〕）＋30×〔Ｃ〕＞3.0
と、8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２
×〔Mn〕＋４×〔Ni〕＋〔Mo〕≦18.0％とを満たし、残
部がFeおよび不可避的不純物からなる熱延マルテンサイ
ト系ステンレス鋼板または、冷延マルテンサイト系ステ
ンレス鋼板である。Means for Solving the Problems The martensitic stainless steel sheet according to the present invention has a composition of steel sheet or composition of molten steel in mass%, C: less than 0.02%, Si: 1.0% or less, Mn: 1.
Less than 5%, P: 0.04% or less, S: 0.01% or less, Al: 0.1
% Or less, Ni: 1.5% or more, less than 4.0%, Cr: 11% or more,
Less than 15%, Mo: 0.5% or more, less than 2.0%, N: less than 0.02%, 15.0% ≦ [Cr] + 1.5 × [Mo] + 1.2 ×
[Ni] ≦ 20.0%, [C] + [N] <0.030%, [N
i] + 0.5 x ([Mn] + [Mo]) + 30 x [C]> 3.0
And 8.0% ≦ 72 × [C] + 40 × [N] + 3 × [Si] +2
It is a hot-rolled martensitic stainless steel sheet or a cold-rolled martensitic stainless steel sheet with the balance of [Mn] + 4 × [Ni] + [Mo] ≦ 18.0% and the balance being Fe and inevitable impurities.
【０００９】またさらに、Cu、Coの一方または両方がC
u：2.0 ％以下、Co：2.0 ％以下添加され、かつ上記不
等式の代わりに、15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2
×〔Ni〕＋0.5 ×〔Cu〕＋0.3 ×〔Co〕≦20.0％と、
〔Ｃ〕＋〔Ｎ〕＜0.03％と、〔Ni〕＋0.5 ×( 〔Mn〕＋
〔Mo〕＋〔Cu〕）＋30×〔Ｃ〕＞3.0 と、8.0 ％≦72×
〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕＋４×
〔Ni〕＋〔Mo〕＋〔Cu〕＋0.8 ×〔Co〕≦18.0％とを満
たすようにしてもよい。Furthermore, one or both of Cu and Co are C
u: 2.0% or less, Co: 2.0% or less, and 15.0% ≦ [Cr] + 1.5 × [Mo] +1.2 instead of the above inequality.
X [Ni] + 0.5 x [Cu] + 0.3 x [Co] ≤ 20.0%,
[C] + [N] <0.03% and [Ni] + 0.5 × ([Mn] +
[Mo] + [Cu]) + 30 × [C]> 3.0 and 8.0% ≦ 72 ×
[C] + 40 × [N] + 3 × [Si] + 2 × [Mn] + 4 ×
[Ni] + [Mo] + [Cu] + 0.8 × [Co] ≦ 18.0% may be satisfied.
【００１０】あるいはさらに、Ti、Nb、Ｖ、Zr、Taのう
ちから選ばれる１種または２種以上がTi：0.2 ％以下、
Nb：0.2 ％以下、Ｖ：0.2 ％以下、Zr：0.2 ％以下、T
a：0.2 ％以下添加してもよい。またさらに、Ｂ、Caの
一方または両方がＢ：0.005 ％以下、Ca：0.005 ％以下
添加してもよい。もしくは、Ｗ、Mgの一方または両方が
Ｗ：0.1 ％以下、Mg：0.01％以下添加されてなるように
してもよい。Alternatively, one or more selected from Ti, Nb, V, Zr and Ta may have a Ti content of 0.2% or less,
Nb: 0.2% or less, V: 0.2% or less, Zr: 0.2% or less, T
a: 0.2% or less may be added. Further, one or both of B and Ca may be added in an amount of B: 0.005% or less and Ca: 0.005% or less. Alternatively, one or both of W and Mg may be added with W: 0.1% or less and Mg: 0.01% or less.
【００１１】上記いずれの場合でも、熱延鋼板および冷
延鋼板の引張強度が600MPa超え、900MPa未満であること
が好ましい。また、上記の鋼板は、車両構造用材料に使
用されるのが好ましい。また、上記鋼板の製造方法であ
る。なお、上記の〔元素記号〕は元素の質量％を示す。
以下、同様とする。In any of the above cases, it is preferable that the hot-rolled steel sheet and the cold-rolled steel sheet have a tensile strength of more than 600 MPa and less than 900 MPa. Further, the above steel plate is preferably used as a material for vehicle structure. Moreover, it is a manufacturing method of the said steel plate. In addition, the above [elemental symbol] shows the mass% of the element.
The same applies hereinafter.
【００１２】[0012]
【発明の実施の形態】本発明者らは、上記の目的を達成
すべく、マルテンサイト系ステンレス鋼板の成分が耐食
性、溶接部の靱性に加え、加工性に及ぼす影響について
詳細に調査し、（１）から（４）の知見に基づいてマル
テンサイト系ステンレス鋼板の成分を適正化した。
（１）Mo、Niの適正な添加により、質量％で11％以上15
％未満のCrを含有する鋼板の耐食性が顕著に改善され
る、（２）Ｃ、Ｎの含有量を極めて少なくすることによ
り、加工性と溶接部靱性が顕著に向上する、（３）Ｃ、
Mn、Ni、Moを適正範囲に制御することにより、焼き入れ
性が高められ、高強度が得られる、（４）上記（１）〜
（３）の効果が十分得られる範囲でＣ、Ｎ、Si、Mn、N
i、Moを適正範囲に制御することにより、高強度と高加
工性を両立させることができることを新たに見出した。BEST MODE FOR CARRYING OUT THE INVENTION In order to achieve the above-mentioned object, the present inventors investigated in detail the influence of the components of a martensitic stainless steel sheet on the workability as well as the corrosion resistance and the toughness of the welded part. The components of the martensitic stainless steel sheet were optimized based on the findings of 1) to (4). (1) With proper addition of Mo and Ni, 11% or more by mass% 15
%, The corrosion resistance of the steel sheet containing Cr is significantly improved. (2) By significantly reducing the contents of C and N, the workability and weld toughness are significantly improved, (3) C,
By controlling Mn, Ni, and Mo in appropriate ranges, hardenability is enhanced and high strength is obtained. (4) Above (1)-
C, N, Si, Mn, N within the range where the effect of (3) is sufficiently obtained
It has been newly found that high strength and high workability can be achieved by controlling i and Mo in appropriate ranges.
【００１３】以下、本発明のマルテンサイト系ステンレ
ス鋼板（以下、「本発明の鋼板」という）について詳細
に説明する。まず、本発明の鋼板における成分限定理由
について説明する。成分含有量、添加量等は質量％とす
る。
Ｃ：0.02％未満
Ｃは、加工性および溶接部靱性を低下させ、また溶接割
れ感受性を高める元素であり、含有量が0.02質量％以上
になると、その悪影響が顕著となるので、0.02質量％未
満に限定する。特に、溶接部靱性の観点から、上限は0.
010 質量％未満とすることが望ましい。一方でＣは鋼板
の強度を高める元素であり、高強度化のために、0.005
質量％を超えて添加することが望ましい。The martensitic stainless steel sheet of the present invention (hereinafter referred to as the "steel sheet of the present invention") will be described in detail below. First, the reasons for limiting the components in the steel sheet of the present invention will be described. The content of components, the amount of addition, and the like are mass%. C: less than 0.02% C is an element that lowers the workability and toughness of the welded portion and increases the susceptibility to welding cracks. If the content is 0.02% by mass or more, the adverse effect becomes remarkable, so less than 0.02% by mass. Limited to Especially, from the viewpoint of weld toughness, the upper limit is 0.
It is desirable that the content is less than 010% by mass. On the other hand, C is an element that enhances the strength of the steel sheet.
It is desirable to add more than mass%.
【００１４】Si：1.0 ％以下
Siは、脱酸剤として必要な元素であるとともに、鋼板の
強度を高める元素である。その効果を得るためには、少
なくとも0.1 質量％以上の添加が必要である。しかしな
がら1.0 質量％を超えると鋼板の伸びを低下させるとと
もに脆化させ、加工性および溶接部靱性を低下させるこ
とから、1.0 質量％を上限とする。溶接部靱性の観点か
ら、0.3 質量％以下の添加が望ましい。Si: 1.0% or less Si is an element necessary as a deoxidizing agent and also an element for increasing the strength of the steel sheet. In order to obtain the effect, it is necessary to add at least 0.1 mass% or more. However, if it exceeds 1.0 mass%, the elongation of the steel sheet is reduced and embrittlement is caused, and the workability and weld toughness are deteriorated. Therefore, the upper limit is 1.0 mass%. From the viewpoint of weld toughness, addition of 0.3 mass% or less is desirable.
【００１５】Mn：1.5 ％未満
Mnは、マルテンサイト系ステンレス鋼板の特徴である高
温（およそ1000〜1100℃）でのオーステナイト相を得る
ために必要である。このオーステナイト相は空冷により
微細なマルテンサイト組織に変態するため、溶接熱影響
部において靱性向上に寄与する。その効果を得るために
は、少なくとも0.1 質量％以上の添付が必要である。し
かし、過剰に添加すると鋼板の加工性および耐食性を低
下させることから、1.5 質量％未満に限定する。鋼板の
加工性および耐食性の観点からは、0.5 質量％以下の添
加が望ましい。Mn: less than 1.5% Mn is necessary to obtain the austenite phase at high temperatures (approximately 1000 to 1100 ° C.), which is a characteristic of martensitic stainless steel sheets. Since this austenite phase is transformed into a fine martensitic structure by air cooling, it contributes to the improvement of toughness in the weld heat affected zone. To obtain the effect, at least 0.1 mass% or more must be attached. However, if added excessively, the workability and corrosion resistance of the steel sheet will be reduced, so the content is limited to less than 1.5% by mass. From the viewpoint of workability and corrosion resistance of steel sheet, addition of 0.5 mass% or less is desirable.
【００１６】Ｐ：0.04％以下
Ｐは、鋼の加工性を低下させる元素であり、出来る限り
低い方が好ましいが、あまりに低くすることは製鋼のコ
ストの上昇を招くため0.04質量％を上限とする。加工性
の観点からは、含有量を0.02質量％以下にすることが望
ましい。
Ｓ：0.01％以下
Ｓは、耐食性を低下させる元素であり、出来る限り低い
方が好ましいが、製鋼時の脱Ｓ処理にかかる経済的制限
から、0.01質量％以下とする。耐食性の観点からは、含
有量を0.003 質量％以下にすることが望ましい。P: 0.04% or less P is an element that deteriorates the workability of steel, and it is preferable that it is as low as possible, but if it is made too low, the cost of steelmaking will increase, so 0.04 mass% is the upper limit. . From the viewpoint of workability, it is desirable that the content be 0.02 mass% or less. S: 0.01% or less S is an element that lowers the corrosion resistance and is preferably as low as possible, but is 0.01% by mass or less because of the economic limitation on the de-S treatment during steelmaking. From the viewpoint of corrosion resistance, the content is preferably 0.003 mass% or less.
【００１７】Al：0.1 ％以下
Alは製鋼上脱酸剤として必要である。その効果を得るた
めには少なくとも0.002 質量％以上の添加が必要であ
る。しかし、過剰に添加すると介在物の生成により耐食
性および靱性が低下するため、0.1 質量％以下に限定す
る。溶接部靱性確保の観点からは、0.05質量％以下とす
ることが好ましい。Al: 0.1% or less Al is necessary as a deoxidizer for steelmaking. In order to obtain the effect, it is necessary to add at least 0.002 mass% or more. However, if added excessively, the corrosion resistance and toughness will decrease due to the formation of inclusions, so the content is limited to 0.1 mass% or less. From the viewpoint of ensuring the toughness of the welded portion, it is preferably 0.05% by mass or less.
【００１８】Ni：1.5 ％以上、4.0 ％未満
Niは、ステンレス鋼板の特徴である耐食性を向上させ、
母材および溶接部の靱性を向上させる効果をもつ。ま
た、マルテンサイト系ステンレス鋼板の特徴である高温
でのオーステナイト相を得るために必要である。この効
果を得るために、1.5 質量％以上添加する。一方、4.0
質量％以上添加すると鋼板が顕著に硬化し、伸びが低下
するため、4.0 質量％未満の範囲で添加する。耐食性の
観点からは、2.0 質量％以上添加することが好ましい。
また、3.0 質量％以下の添加でも耐食性改善効果は十分
に現れる。Ni: 1.5% or more and less than 4.0% Ni improves the corrosion resistance, which is a characteristic of stainless steel sheets,
It has the effect of improving the toughness of the base material and the weld. It is also necessary to obtain the austenite phase at high temperature, which is a characteristic of martensitic stainless steel sheets. To obtain this effect, it is added in an amount of 1.5% by mass or more. On the other hand, 4.0
If it is added in an amount of more than 100% by mass, the steel sheet will be significantly hardened and the elongation will be reduced. Therefore, it is added in an amount less than 4.0% by mass. From the viewpoint of corrosion resistance, it is preferable to add 2.0% by mass or more.
Further, the addition of 3.0% by mass or less sufficiently shows the effect of improving the corrosion resistance.
【００１９】Cr：11％以上、15％未満、
Crはステンレス鋼の特徴である耐食性の向上に有効な元
素成分であり、十分な耐食性を得るためには11質量％以
上が必要であり、これを下限とする。耐食性の観点から
は、Crは12質量％以上添加することが好ましく、13質量
％以上添加することがより好ましい。一方、Crは鋼板の
靱性を低下させ、特に15質量％以上添加すると靱性の低
下が著しくなるため、15質量％未満に限定する。靱性の
観点から、Crは14質量％以下とすることが望ましい。Cr: 11% or more and less than 15%, Cr is an elemental component effective in improving the corrosion resistance characteristic of stainless steel, and 11% by mass or more is necessary to obtain sufficient corrosion resistance. Is the lower limit. From the viewpoint of corrosion resistance, Cr is preferably added in an amount of 12 mass% or more, more preferably 13 mass% or more. On the other hand, Cr reduces the toughness of the steel sheet, and particularly when added in an amount of 15% by mass or more, the toughness is significantly deteriorated, so the content is limited to less than 15% by mass. From the viewpoint of toughness, Cr is preferably 14% by mass or less.
【００２０】Mo：0.5 ％以上、2.0 ％未満
Moは耐食性の向上に特に有効な元素成分であり、0.5 質
量％以上添加する。一方、2.0 質量％以上添加しても、
耐食性向上の効果が飽和するばかりでなく、靱性を低下
させるため、2.0 質量％未満添加する。耐食性の観点か
らは、1.0 質量％以上添加させることが好ましく、また
靱性の観点からは、1.5 質量％未満添加することが好ま
しい。Mo: 0.5% or more and less than 2.0% Mo is a particularly effective elemental component for improving the corrosion resistance, and 0.5% by mass or more is added. On the other hand, even if 2.0 mass% or more is added,
Not only is the effect of improving corrosion resistance saturated, but the toughness is reduced, so less than 2.0% by mass is added. From the viewpoint of corrosion resistance, it is preferable to add 1.0 mass% or more, and from the viewpoint of toughness, it is preferable to add less than 1.5 mass%.
【００２１】Ｎ：0.02％未満
Ｎは、Ｃと同様に加工性および溶接部靱性を低下させ、
また溶接割れ感受性を高める元素であり、含有量が0.02
質量％以上になるとその悪影響が顕著となるので、0.02
質量％未満に限定する。特に、加工性および溶接部靱性
の観点から、0.012 質量％以下とするのが好ましく、0.
008 質量％未満とすることがより好ましい。N: less than 0.02% N, like C, deteriorates workability and weld toughness,
It is an element that increases the sensitivity to welding cracks, and its content is 0.02
If the content is more than 100% by mass, the adverse effect will be significant, so 0.02
Limit to less than mass%. Particularly, from the viewpoint of workability and weld zone toughness, it is preferably 0.012 mass% or less, and
More preferably, it is less than 008% by mass.
【００２２】そのうえ、本発明では、下の（１）〜
（４）式を満たすことを必須とする。
15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕≦20.0％ ・・・（１）
〔Ｃ〕＋〔Ｎ〕＜0.030 ％（好ましくは＜0.015 ％） ・・・（２）
〔Ni〕＋0.5 ×（〔Mn〕＋〔Mo〕）＋30×〔Ｃ〕＞3.0 ・・・（３）
8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕
＋２×〔Mn〕＋４×〔Ni〕＋〔Mo〕≦18.0％ ・・・（４）
（１）式は耐食性および加工性からの限定である。ここ
で、〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕が15.0％未満
の場合、耐食性がSUS301L やSUS304等のオーステナイト
系ステンレス鋼板よりも劣るようになり、一方、〔Cr〕
＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕が20.0％を超えた場合に
は、耐食性改善の効果は飽和し、かつ高合金化による加
工性の低下が顕著になる。このため、耐食性および加工
性の観点から、〔Cr〕並びに〔Mo〕及び〔Ni〕が式
（１）を満たすことを条件とする。Moreover, in the present invention, the following (1) to
It is essential to satisfy the equation (4). 15.0% ≦ [Cr] + 1.5 × [Mo] + 1.2 × [Ni] ≦ 20.0% ・ ・ ・ (1) [C] + [N] <0.030% (preferably <0.015%) ・ ・ ・ ( 2) [Ni] + 0.5 x ([Mn] + [Mo]) + 30 x [C]> 3.0 (3) 8.0% ≤ 72 x [C] + 40 x [N] + 3 x [Si] + 2 × [Mn] + 4 × [Ni] + [Mo] ≦ 18.0% (4) Equation (1) is limited by corrosion resistance and workability. Here, when [Cr] + 1.5 x [Mo] + 1.2 x [Ni] is less than 15.0%, the corrosion resistance becomes inferior to that of austenitic stainless steel sheets such as SUS301L and SUS304, while [Cr]
When + 1.5 × [Mo] + 1.2 × [Ni] exceeds 20.0%, the effect of improving the corrosion resistance is saturated, and the workability due to high alloying is markedly reduced. Therefore, from the viewpoint of corrosion resistance and workability, [Cr] and [Mo] and [Ni] satisfy the condition (1).
【００２３】なお、本発明の鋼板が目標とする耐食性
は、後述の実施例１に記載した複合サイクル腐食試験
（CCT(Cyclic Corrosion Test)）での発錆面積率が30％
以下で、かつ発錆最大穴深さが100 μｍ以下である。こ
れを達成する場合には、特に車両構造用として十分な耐
食性を示す。また、本発明の鋼板が目標とする加工性
は、後述の実施例１に記載した引張試験での伸びが25％
以上、曲げ試験での割れがないことである。これを達成
する場合には、特に車両構造用として十分な加工性を示
す。The target corrosion resistance of the steel sheet of the present invention is that the rusting area ratio in the combined cycle corrosion test (CCT (Cyclic Corrosion Test)) described in Example 1 described later is 30%.
And the maximum rusting hole depth is 100 μm or less. When this is achieved, it exhibits sufficient corrosion resistance, especially for vehicle construction. Further, the workability targeted for the steel sheet of the present invention is that the elongation in the tensile test described in Example 1 described later is 25%.
As mentioned above, there is no crack in the bending test. When this is achieved, it exhibits sufficient workability, especially for vehicle construction.
【００２４】（２）式は加工性および溶接部靱性からの
限定である。〔Ｃ〕＋〔Ｎ〕が0.030 ％を超えると、加
工性、溶接部靱性が極めて悪化する。そこで、加工性お
よび溶接部靱性の観点から〔Ｃ〕及び〔Ｎ〕が式（２）
を満たすことを条件とする。なお、加工性および溶接部
靱性の両方を顕著に改善するには、〔Ｃ〕＋〔Ｎ〕が0.
015 ％未満であることが好ましい。Equation (2) is a limitation due to workability and weld toughness. When [C] + [N] exceeds 0.030%, workability and weld toughness are extremely deteriorated. Therefore, from the viewpoint of workability and weld toughness, [C] and [N] are expressed by the formula (2).
The condition is to satisfy. In order to significantly improve both workability and weld toughness, [C] + [N] is 0.
It is preferably less than 015%.
【００２５】なお、本発明の鋼板が、目標とする加工性
は、（１）式の説明において前述したとおりである。引
張試験の破断伸びが25％以上で、かつ曲げ試験結果が割
れ無しであり、この場合には、加工性に優れ、特に車両
構造用として用いることができる。また、本発明の鋼板
が、目標とする溶接部靱性は、後述の実施例１に記載し
たシャルピー衝撃試験で測定される溶接熱影響部のシャ
ルピー衝撃値（v E −50℃）が50J/cm2 以上であり、こ
の場合、特に車両構造用として靱性が十分である。The target workability of the steel sheet of the present invention is as described above in the explanation of the equation (1). The breaking elongation in the tensile test is 25% or more, and the bending test result shows no cracking. In this case, the workability is excellent, and it can be used particularly for vehicle structure. In addition, the steel sheet of the present invention has a target welded toughness in which the Charpy impact value ( v E −50 ° C.) of the weld heat affected zone measured by the Charpy impact test described in Example 1 described later is 50 J / cm. It is 2 or more, and in this case, the toughness is sufficient especially for a vehicle structure.
【００２６】（３）式は、焼き入れ性（引張強度）から
の限定である。〔Ni〕＋0.5 ×（〔Mn〕＋〔Mo〕）＋30
×〔Ｃ〕が3.0 以下であると、900 ℃〜1100℃で生じる
オーステナイト相の体積率が80％以下となり、焼き入
れ、焼き戻しによる高強度化ができなくなる。なお、本
発明の鋼板が目的とする強度は、引張試験での引張強度
が600MPa超えであり、これを達成する場合には、特に車
両構造用として十分な強度を示す。The expression (3) is limited by the hardenability (tensile strength). [Ni] +0.5 x ([Mn] + [Mo]) + 30
When x [C] is 3.0 or less, the volume ratio of the austenite phase generated at 900 ° C. to 1100 ° C. is 80% or less, and the strength cannot be increased by quenching and tempering. The target strength of the steel sheet of the present invention is a tensile strength of more than 600 MPa in a tensile test, and when this is achieved, it exhibits sufficient strength particularly for vehicle structures.
【００２７】（４）式は引張強度および加工性からの限
定である。72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×
〔Mn〕＋４×〔Ni〕＋〔Mo〕が8.0 ％未満の場合、室温
での引張強度が600MPa未満となり、一方、72×〔Ｃ〕＋
40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕＋４×〔Ni〕＋
〔Mo〕が18.0％を超えると、鋼が過度に高合金化し、室
温での引張強度が900MPa以上となり、本発明の目標とす
る加工性が得られなくなる。そこで加工性の観点から、
〔Ｃ〕、〔Ｎ〕、〔Si〕、〔Mn〕、〔Ni〕及び〔Mo〕が
式（４）を満たすことを条件とする。Equation (4) is a limitation due to tensile strength and workability. 72 x [C] + 40 x [N] + 3 x [Si] + 2 x
When [Mn] + 4 × [Ni] + [Mo] is less than 8.0%, the tensile strength at room temperature is less than 600 MPa, while 72 × [C] +
40 x [N] + 3 x [Si] + 2 x [Mn] + 4 x [Ni] +
When [Mo] exceeds 18.0%, the steel becomes excessively alloyed and the tensile strength at room temperature becomes 900 MPa or more, and the workability targeted by the present invention cannot be obtained. So from the viewpoint of workability,
The condition is that [C], [N], [Si], [Mn], [Ni], and [Mo] satisfy the formula (4).
【００２８】なお、本発明の鋼板が目標とする強度は、
引張試験での引張強度が600MPa超え、900MPa未満であ
る。室温での引張強度が600MPa以下であれば車両構造用
として不十分であり、一方、室温での引張強度が900MPa
以上になると車両構造体としての強度は確保されるが、
加工が著しく困難となるため、900MPa未満に限定する。
上記の特性（耐食性、加工性、溶接部靱性および引張強
度）のいずれか一つでも満足していない場合、車両構造
用として用いることができない。The target strength of the steel sheet of the present invention is
The tensile strength in the tensile test is more than 600 MPa and less than 900 MPa. If the tensile strength at room temperature is 600 MPa or less, it is insufficient for vehicle structure, while the tensile strength at room temperature is 900 MPa.
If the above, the strength as a vehicle structure is secured,
Since it is extremely difficult to process, limit it to less than 900MPa.
If any one of the above properties (corrosion resistance, workability, weld toughness and tensile strength) is not satisfied, it cannot be used for a vehicle structure.
【００２９】また本発明の鋼板は、上記成分以外はFeお
よび不可避的不純物である。但し、アルカリ金属、アル
カリ土類金属、希土類元素および遷移金属などがそれぞ
れ、0.1 質量％以下と少量含有されてもよい。これらの
元素の少量の含有は、本発明の効果を何ら妨げるもので
はない。また、本発明においては、（Cu、Co）並びに
（Ti、Nb、Ｖ、Zr、Ta）、（Ｂ、Ca）および（Ｗ、Mg）
は必須成分ではないが、以下の範囲で添加することがで
きる。The steel sheet of the present invention contains Fe and unavoidable impurities other than the above components. However, alkali metals, alkaline earth metals, rare earth elements, transition metals and the like may be contained in small amounts of 0.1% by mass or less. The inclusion of a small amount of these elements does not hinder the effects of the present invention. Further, in the present invention, (Cu, Co) and (Ti, Nb, V, Zr, Ta), (B, Ca) and (W, Mg)
Is not an essential component, but can be added within the following range.
【００３０】Cu、Coは、Moと同様に耐食性の向上に有効
な元素成分であり、十分な耐食性改善効果を得るために
は、一方または両方を0.02質量％以上、さらに好ましく
は0.3 質量％以上添加することが好ましい。それぞれ2.
0 質量％を超えて添加すると、効果が飽和するばかりで
なく、加工性および靱性を低下させるため、Cu、Coの一
方または両方をCu：2.0 ％以下、Co：2.0 ％以下添加す
る。Like Mo, Cu and Co are elemental components effective for improving the corrosion resistance. To obtain a sufficient corrosion resistance improving effect, one or both of them is 0.02 mass% or more, more preferably 0.3 mass% or more. It is preferable to add. 2.
If it is added in an amount of more than 0% by mass, not only the effect will be saturated, but also the workability and toughness will be deteriorated, so one or both of Cu and Co are added at Cu: 2.0% or less and Co: 2.0% or less.
【００３１】その際、このような鋼板においても、
〔Ｃ〕＋〔Ｎ〕が上記（２）式を満たすことを要件とす
る。その理由は、〔Ｃ〕＋〔Ｎ〕が0.030 ％を超える
と、加工性、溶接部靱性が極めて悪化するからである。
そこで、加工性および溶接部靱性の観点から〔Ｃ〕及び
〔Ｎ〕が式（２）を満たすことを条件とする。なお、加
工性および溶接部靱性の両方を顕著に改善するには、
〔Ｃ〕＋〔Ｎ〕が0.015 ％未満であることが好ましい。At this time, even in such a steel plate,
It is required that [C] + [N] satisfy the above expression (2). The reason is that if [C] + [N] exceeds 0.030%, workability and weld toughness are extremely deteriorated.
Therefore, from the viewpoint of workability and weld toughness, [C] and [N] satisfy the condition (2). In order to significantly improve both workability and weld toughness,
[C] + [N] is preferably less than 0.015%.
【００３２】また、（１）、（３）、（４）式に代えて
下記の（５）、（６）、（７）式を満たすようにする必
要がある。但し、（５）、（６）、（７）式の意義は、
それぞれ上述した（１）、（３）、（４）式と同じであ
る。
15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕
＋0.5 ×〔Cu〕＋0.3 ×〔Co〕≦20.0％ ・・・（５）
〔Ni〕＋0.5 ×( 〔Mn〕＋〔Mo〕＋〔Cu〕）＋30×〔Ｃ〕＞3.0 ・・・（６）
8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕
＋４×〔Ni〕＋〔Mo〕＋〔Cu〕＋0.8 ×〔Co〕≦18.0％ ・・・（７）
なお、CuまたはCoのいずれか一方を添加する場合、添加
しない方の添加量が0.02質量％未満の場合は（５）、
（６）、（７）式では０％として扱う。Further, it is necessary to satisfy the following expressions (5), (6) and (7) instead of expressions (1), (3) and (4). However, the significance of equations (5), (6), and (7) is
These are the same as the above-described formulas (1), (3), and (4), respectively. 15.0% ≦ [Cr] + 1.5 × [Mo] + 1.2 × [Ni] + 0.5 × [Cu] + 0.3 × [Co] ≦ 20.0% ・ ・ ・ (5) [Ni] + 0.5 × ([Mn] + [Mo] + [Cu]) + 30 × [C]> 3.0 ・ ・ ・ (6) 8.0% ≦ 72 × [C] + 40 × [N] + 3 × [Si] + 2 × [Mn] +4 × [Ni] + [Mo] + [Cu] +0.8 × [Co] ≦ 18.0% (7) When either Cu or Co is added, the addition amount is 0.02. If it is less than mass% (5),
It is treated as 0% in the equations (6) and (7).
【００３３】Ti、Nb、Ｖ、Zr、Taは、微量の添加により
鋼板の加工性を高くする元素であり、必要に応じてそれ
ぞれ 0.2質量％を上限として添加する。その効果を得る
ためには、それぞれ0.02質量％以上添加する。しかしな
がら、それぞれ0.2 質量％を超えて添加すると過度に硬
化し、加工性が低下するため、Ti、Nb、Ｖ、Zr、Taのう
ちから選ばれる１種または２種以上をそれぞれ、0.2 質
量％以下添加する。Ti, Nb, V, Zr, and Ta are elements that improve the workability of the steel sheet by adding a trace amount, and if necessary, 0.2 mass% is added as the upper limit, respectively. To obtain the effect, 0.02 mass% or more is added to each. However, if added in excess of 0.2% by mass, the composition will be excessively hardened and the workability will be deteriorated. Therefore, one or more selected from Ti, Nb, V, Zr and Ta should be 0.2% by mass or less, respectively. Added.
【００３４】Ｂ、Caは、微量の添加で鋼板の強度を高く
する効果があり、必要に応じて添加する。その効果を得
るためには、0.0005質量％以上添加する。しかしなが
ら、それぞれ0.005 質量％を超えて添加しても効果が飽
和するばかりでなく、耐食性を低下させるため、Ｂ、Ca
の一方または両方を0.005 質量％以下添加する。Ｗ、Mg
は鋼板の強度を高くする効果があるため、必要に応じて
添加する。その効果を得るためには、Ｗは0.01質量％以
上、Mgは0.001 質量％以上添加する。しかしながら、Ｗ
は 0.1質量％を超えて含有すると靱性を低下させ、Mgは
0.01質量％を超えて含有すると靱性を低下させるため、
Ｗ、Mgの一方または両方をＷ： 0.1質量％以下、Mg：0.
01質量％以下添加する。B and Ca have the effect of increasing the strength of the steel sheet even if added in a trace amount, and are added as necessary. To obtain the effect, 0.0005 mass% or more is added. However, addition of more than 0.005% by mass not only saturates the effect but also lowers the corrosion resistance.
Add 0.005% by mass or less of one or both of them. W, Mg
Has the effect of increasing the strength of the steel sheet, so it is added if necessary. In order to obtain the effect, W is added by 0.01 mass% or more and Mg is added by 0.001 mass% or more. However, W
Content of more than 0.1 mass% reduces toughness, and Mg is
If the content exceeds 0.01% by mass, the toughness decreases, so
One or both of W and Mg, W: 0.1 mass% or less, Mg: 0.
Add up to 01 mass%.
【００３５】本発明が目標とする鋼板の特性について下
記にまとめて説明する。
（１）耐食性：後述の実施例１に記載の複合サイクル腐
食試験(CCT(Cyclic Corrosion Test))での発錆面積率が
30％以下で、かつ発錆最大穴深さが100 μｍ以下であ
り、特に車両構造用として十分な耐食性を示す。
（２）加工性：後述の実施例１に記載の引張試験での伸
びが25％以上、かつ曲げ試験での割れがなく、特に車両
構造用として十分な加工性を示す。
（３）溶接部靱性：後述の実施例１に記載のシャルピー
衝撃試験で測定される溶接熱影響部のシャルピー衝撃値
（v E-50℃）が50J/cm2 以上であり、特に車両構造用と
して靱性が十分である。
（４）引張強度：600MPa超え、900MPa未満である。引張
強度が600MPaを超えるため、特に車両構造用として十分
な引張強度を示す。また、引張強度が900MPa未満であ
り、25％以上の破断伸びが、特に車両構造用として曲げ
加工等の加工性にも優れる。The characteristics of the steel sheet targeted by the present invention will be summarized below. (1) Corrosion resistance: The rusted area ratio in the combined cycle corrosion test (CCT (Cyclic Corrosion Test)) described in Example 1 below is
It has a corrosion resistance of 30% or less and a maximum rusting hole depth of 100 μm or less, and exhibits sufficient corrosion resistance especially for vehicle structures. (2) Workability: Elongation in a tensile test described in Example 1 described later is 25% or more, and there is no crack in a bending test, and the workability is particularly sufficient for a vehicle structure. (3) Weld toughness: The Charpy impact value ( v E-50 ° C) of the weld heat affected zone measured by the Charpy impact test described in Example 1 below is 50 J / cm 2 or more, especially for vehicle structures. As toughness is sufficient. (4) Tensile strength: more than 600 MPa and less than 900 MPa. Since the tensile strength exceeds 600 MPa, it exhibits sufficient tensile strength especially for vehicle structures. Further, it has a tensile strength of less than 900 MPa, a breaking elongation of 25% or more, and excellent workability such as bending especially for vehicle structures.
【００３６】本発明の鋼板を製造する方法は、溶鋼の段
階で上述するような溶鋼の組成を成分調整する以外は特
に限定されず、マルテンサイト系ステンレス鋼板の製造
に一般的に採用されている方法をそのまま適用すること
ができる。例えば、転炉あるいは電気炉等を持つ製鋼で
は、上記の必須成分を含有する鋼に必要に応じて添加さ
れる成分を添加して溶鋼の組成を本発明で規定した範囲
内に成分調整して溶製し、VOD （Vacuum Oxygen Decarb
urization ）あるいはAOD（Argon Oxygen Decarburizat
ion）により２次精錬を行う方法が好適である。溶製し
た溶鋼は、公知の鋳造方法にしたがってスラブとするこ
とができる。スラブとするには、生産性および品質の観
点から、連続鋳造法を適用するのが好ましい。連続鋳造
して得られた鋼スラブは、1000〜1250℃に加熱され、通
常の条件の熱間圧延により所望の板厚1.5 〜8.0mm の熱
延板とされる。この熱延板は、必要に応じ好ましくは60
0 〜800 ℃のバッチ式焼鈍を施した後、酸洗等により脱
スケールされ熱延板製品となる。また、用途によって
は、冷間圧延を施し、700 〜800℃の連続焼鈍及び酸洗
を施して、板厚0.3 〜3.0mm の冷延焼鈍板製品とされ
る。The method for producing the steel sheet of the present invention is not particularly limited except for adjusting the composition of the molten steel as described above in the molten steel stage, and is generally adopted for producing martensitic stainless steel sheets. The method can be applied as is. For example, in steel making with a converter or an electric furnace, the composition of molten steel is adjusted within the range specified in the present invention by adding the components added as necessary to the steel containing the above essential components. VOD (Vacuum Oxygen Decarb)
urization) or AOD (Argon Oxygen Decarburizat
A method of performing secondary refining with ion) is preferable. The melted molten steel can be made into a slab according to a known casting method. To form a slab, it is preferable to apply a continuous casting method from the viewpoint of productivity and quality. The steel slab obtained by continuous casting is heated to 1000 to 1250 ° C. and hot-rolled under normal conditions to obtain a hot-rolled sheet having a desired sheet thickness of 1.5 to 8.0 mm. This hot rolled sheet is preferably 60 if necessary.
After being subjected to batch annealing at 0 to 800 ° C, it is descaled by pickling or the like to obtain a hot rolled sheet product. In addition, depending on the application, cold rolling, continuous annealing at 700 to 800 ° C and pickling are performed to obtain cold rolled annealed sheet products with a sheet thickness of 0.3 to 3.0 mm.
【００３７】このようにして製造して得た熱延板製品あ
るいは冷延焼鈍板製品は、それぞれの用途に応じた曲げ
加工が施されてパイプ、パネル等に成形される。これら
のパイプ、パネル等は、鉄道車両の構造部材や自動車、
バスなどの構造部材として用いられる。これらの構造部
材を溶接するための溶接方法は、特に限定されず、MIG
、MAG 、TIG 等のアーク溶接方法やスポット溶接、シ
ーム溶接等の抵抗溶接方法、および電縫溶接方法などの
高周波抵抗溶接、高周波誘導溶接が適用可能である。そ
の際、本発明の鋼板は、Ｃ、Ｎを低減し、溶接割れを防
止しているため、溶接後の熱処理を行わなくても十分使
用可能である。但し、強度の調整などのために溶接後の
熱処理を行っても良い。The hot-rolled sheet product or the cold-rolled annealed sheet product obtained by the above-mentioned process is bent into a pipe, a panel or the like by being subjected to a bending process according to each application. These pipes and panels are used for structural members of railway vehicles, automobiles,
It is used as a structural member such as a bus. The welding method for welding these structural members is not particularly limited, and MIG
, Arc welding method such as MAG, TIG, resistance welding method such as spot welding and seam welding, and high frequency resistance welding such as electric resistance welding method and high frequency induction welding can be applied. At that time, since the steel sheet of the present invention reduces C and N and prevents weld cracking, it can be sufficiently used without heat treatment after welding. However, heat treatment after welding may be performed to adjust the strength.
【００３８】[0038]
【実施例】（実施例１） 熱延板について調査した結果
を示す。表１、表２に示す化学組成を有する50kg鋼塊を
真空溶解炉で溶製し、1200℃に加熱後、リバース圧延機
による熱間圧延により厚さ３mmの熱延板とし、その後、
650 ℃×15時間の焼鈍を施し、徐冷した後、酸洗で脱ス
ケールし、供試材とした。[Examples] (Example 1) The results of investigations on hot-rolled sheets are shown. A 50 kg steel ingot having the chemical composition shown in Table 1 and Table 2 was melted in a vacuum melting furnace, heated to 1200 ° C., and then hot-rolled by a reverse rolling mill to form a hot-rolled sheet having a thickness of 3 mm, and thereafter,
It was annealed at 650 ° C for 15 hours, gradually cooled, and then descaled by pickling to obtain a test material.
【００３９】[0039]
【表１】 [Table 1]
【００４０】[0040]
【表２】 [Table 2]
【００４１】供試材の耐食性は、JIS Z 2371に準拠した
塩水噴霧と、乾燥、湿潤を組み合わせたサイクル試験
（CCT ）を実施し、調査した。供試材より、寸法70mm×
150 mmの板を採取し、片方の面を試験面として塩水噴
霧：35℃、２時間→乾燥：60℃、４時間→湿潤：50℃、
２時間の塩水噴霧と乾燥、湿潤を組み合わせた合計８時
間のサイクル試験を30サイクル行ったのち、コンピュー
タによる画像解析により試験面の発錆面積を求め、試験
面で徐して発錆面積を算出し、試験片２枚の平均値をCC
T 発錆面積率とした。The corrosion resistance of the test materials was investigated by carrying out a cycle test (CCT) in which salt spray in accordance with JIS Z 2371 and drying and wetting were combined. From the test material, size 70 mm ×
A 150 mm plate was sampled, with one side as the test surface, salt spray: 35 ° C, 2 hours → drying: 60 ° C, 4 hours → wet: 50 ° C,
After conducting a cycle test of a total of 8 hours, which is a combination of salt spray for 2 hours, drying and wetting, for 30 cycles, the rust area on the test surface is determined by image analysis by a computer, and the rust area is gradually calculated on the test surface. Then, the average value of two test pieces is CC
The ratio of rusted area was T.
【００４２】またさらに、板厚方向の腐食の進行を確認
するために、温度50℃の30質量％硝酸に８時間浸漬して
試験面の錆を除去し、錆の深さの最大値を触針法により
測定し、CCT 発錆最大穴深さとした。引張試験は、供試
材より試験片（JIS Z 2201の13号Ｂ形状）素材の長手方
向が圧延方向となるように採取し、13号Ｂ形状に機械加
工した後、JIS Z 2241に準拠して試験を行い、圧延方向
の引張強度と破断伸びを測定した。Further, in order to confirm the progress of corrosion in the plate thickness direction, the test surface was immersed in 30% by mass nitric acid at a temperature of 50 ° C. for 8 hours to remove rust, and the maximum rust depth was touched. It was measured by the needle method, and the maximum hole depth of CCT rusting was set. In the tensile test, the test piece (JIS Z 2201 No. 13B shape) was sampled from the test material so that the longitudinal direction of the material was the rolling direction, machined into No. 13B shape, and conformed to JIS Z 2241. The test was carried out to measure the tensile strength and elongation at break in the rolling direction.
【００４３】曲げ試験は、幅25mm×長さ70mmの試験片
を、長手方向が圧延方向と平行になるように採取し、内
側半径1.5 mmの180 度曲げを行い、曲げの外側を拡大鏡
で観察し、割れの有無を調べた。さらに、溶接部の靱性
は、次のようにして評価した。同じ供試材番号の供試材
の圧延方向の板厚面同志を向かい合わせて、突き合わ
せ、図１に示すような溶接方向にMIG 溶接（ワイヤ：JI
S Y308、電流：150A、電圧：19V 、溶接速度：９mm/se
c、シールドガス：100vol％Arを20リットル／分、ルー
トギャップ：１mm）により溶接し、シャルピー衝撃試験
片素材をその長手方向が圧延材の幅方向と平行となるよ
うに採取し、採取した試験片素材を厚みＨが10mm、幅Ｗ
が３mm、長さＬが55mmのシャルピー衝撃試験片に機械加
工により仕上げた。図１には、機械加工後のシャルピー
衝撃試験片の形状を、溶接部位と対応させて示した。機
械加工では、ボンド部から１mm距離離れた溶接熱影響部
に２mmＶノッチ加工を施すと共に溶接余盛を研削で除去
した。In the bending test, a test piece having a width of 25 mm and a length of 70 mm was sampled so that the longitudinal direction was parallel to the rolling direction, 180 ° bending with an inner radius of 1.5 mm, and the outside of the bending with a magnifying glass. It was observed and examined for cracks. Further, the toughness of the welded portion was evaluated as follows. The specimens with the same specimen number are made to face each other in the rolling direction, but face each other, and MIG welding (wire: JI
S Y308, current: 150A, voltage: 19V, welding speed: 9mm / se
c, shield gas: 100 vol% Ar, 20 liter / min, root gap: 1 mm) were welded, the Charpy impact test piece material was sampled so that its longitudinal direction was parallel to the width direction of the rolled material, and the sampled test Thickness H is 10mm, width W is one piece
Was machined into a Charpy impact test piece having a length of 3 mm and a length L of 55 mm. In FIG. 1, the shape of the Charpy impact test piece after machining is shown in correspondence with the welded portion. In machining, a 2 mm V-notch process was applied to the weld heat affected zone 1 mm away from the bond and the weld surplus was removed by grinding.
【００４４】シャルピー衝撃試験は、５本の衝撃試験片
について、JIS Z 2242に準拠し、−50℃での吸収エネル
ギーをそれぞれ測定し、その後、吸収エネルギーをノッ
チ部断面積：Ｈ方向８mm×Ｗ方向３mmで除して、各衝撃
試験片のシャルピー衝撃値（ｖＥ−50℃）を求めた。溶
接部の靱性は、５本の衝撃試験片のシャルピー衝撃値の
平均値を溶接熱影響部のｖＥ−50℃（Ｊ／cm2 ）として
評価した。In the Charpy impact test, the absorbed energy at -50 ° C. was measured for each of the five impact test pieces in accordance with JIS Z 2242, and then the absorbed energy was measured for the notch cross-sectional area: H direction 8 mm × W. The Charpy impact value (vE-50 ° C.) of each impact test piece was obtained by dividing by 3 mm in the direction. The toughness of the weld was evaluated by taking the average value of the Charpy impact values of the five impact test pieces as vE-50 ° C (J / cm 2 ) of the weld heat affected zone.
【００４５】以上の結果を表３、表４に示す。The above results are shown in Tables 3 and 4.
【００４６】[0046]
【表３】 [Table 3]
【００４７】[0047]
【表４】 [Table 4]
【００４８】表３および表４から明らかなごとく、本発
明例の熱延鋼板は、耐食性、溶接部の靱性に加え、加工
性に優れていることが分かる。比較例の熱延鋼板は、耐
食性、溶接部および加工性いずれかが本発明例の熱延鋼
板に比べて劣っている。ここで、CCT 発錆面積率が30％
以下で、かつCCT 発錆最大穴深さが100 μｍ以下の場
合、耐食性が車両構造用として十分であり、また、溶接
熱影響部のｖＥ−50℃が50J/cm2 以上の場合、車両構造
用として靭性が十分である。そのうえ、引張試験の破断
伸びが25％以上で、かつ曲げ試験結果が割れ無しの場合
には、加工性に優れ、車両構造用として用いることがで
きる。上記の特性のいずれか一つでも満足していない場
合、車両構造用として用いることができない。なお、引
張試験の引張強度については、室温での引張強度が600M
Paを超え、900MPa未満として、車両構造体としての強度
を確保した。
（実施例２） 次に、冷延焼鈍板の特性を調査した結果
を示す。As is clear from Tables 3 and 4, the hot-rolled steel sheets of the examples of the present invention are excellent in workability in addition to corrosion resistance and toughness of the welded portion. The hot-rolled steel sheet of the comparative example is inferior to the hot-rolled steel sheet of the inventive example in any of corrosion resistance, welded portion and workability. Where the CCT rusted area ratio is 30%
When the maximum CCT rusting hole depth is 100 μm or less, the corrosion resistance is sufficient for the vehicle structure, and when vE-50 ° C of the weld heat affected zone is 50 J / cm 2 or more, the vehicle structure is It has sufficient toughness for use. In addition, when the elongation at break in the tensile test is 25% or more and the bending test result shows no cracking, the workability is excellent and it can be used for a vehicle structure. If any one of the above characteristics is not satisfied, it cannot be used for vehicle structure. The tensile strength of the tensile test is 600M at room temperature.
The strength as a vehicle structure was secured by exceeding Pa and less than 900 MPa. (Example 2) Next, the result of investigating the characteristics of the cold rolled annealed sheet will be shown.
【００４９】前述の実施例１の表１の供試材番号13の３
mmの熱延板を、リバース圧延機による冷間圧延により板
厚1.5mm になるまで圧延し、750 ℃×１分の焼鈍を行っ
た後、60℃の混酸（硝酸10質量％＋ふっ酸３質量％）に
浸漬して脱スケールして、冷延焼鈍板を得た。前述の実
施例１の熱延板と同様の試験を実施した。ただし、溶接
部靱性を調べるための、溶接はTIG （Tungsten Inert G
as）溶接（電流：95A、電圧：11V 、溶接速度：400 mm/
min、シールドガスは表側（電極側）：20リットル／min
、裏側：10リットル／min ）を用いた。Specimen No. 13-3 in Table 1 of Example 1 described above
A hot-rolled steel sheet having a thickness of 1.5 mm is cold-rolled by a reverse rolling mill to a thickness of 1.5 mm, annealed at 750 ° C for 1 minute, and then mixed at 60 ° C (10% by mass nitric acid + 3% hydrofluoric acid). Mass%) and descaled to obtain a cold rolled annealed plate. The same test as that of the hot-rolled sheet of Example 1 was performed. However, the TIG (Tungsten Inert G
as) Welding (current: 95A, voltage: 11V, welding speed: 400 mm /
min, shield gas front side (electrode side): 20 liters / min
, Back side: 10 l / min) was used.
【００５０】その結果、冷延焼鈍板の耐食性は、CCT 発
錆面積率が、13％、CCT 発錆最大穴深さが35μｍであっ
た。冷延焼鈍板の引張特性は、引張強度が680MPa、破断
伸びが26％であり、冷延焼鈍板の曲げ試験結果は、割れ
無しであった。冷延焼鈍板の溶接熱影響部の靱性は、−
50℃におけるシャルピー衝撃値（vE-50 ℃）が、100J/c
m2であった。As a result, as for the corrosion resistance of the cold rolled annealed sheet, the CCT rusting area ratio was 13% and the CCT rusting maximum hole depth was 35 μm. The tensile properties of the cold rolled annealed sheet were such that the tensile strength was 680 MPa and the elongation at break was 26%, and the bending test result of the cold rolled annealed sheet was that there was no crack. The toughness of the heat-affected zone of the cold rolled annealed sheet is −
Charpy impact value at 50 ℃ (vE-50 ℃) is 100J / c
It was m 2 .
【００５１】実施例２に示した冷延焼鈍板も、車両構造
用鋼板として特性の目標を達成していることが確認でき
た。It was confirmed that the cold-rolled and annealed sheet shown in Example 2 also achieved the characteristic target as a steel sheet for vehicle structure.
【００５２】[0052]
【発明の効果】以上説明したように、本発明の鋼板は、
耐食性、溶接部の靱性に加え、加工性に優れるから、特
に、耐食性、溶接部の靱性に加え、高い曲げ加工性の必
要な車両構造部材として用いることができる。As described above, the steel sheet of the present invention is
Since it has excellent workability in addition to corrosion resistance and toughness of the welded portion, it can be used as a vehicle structural member that requires particularly high bending workability in addition to corrosion resistance and toughness of the welded portion.
【図１】シャルピー衝撃試験片の採取方向及びＶノッチ
位置を示す図である。FIG. 1 is a diagram showing a sampling direction and a V notch position of a Charpy impact test piece.
Ｌ シャルピー衝撃試験片の長さ Ｈ シャルピー衝撃試験片の厚み Ｗ シャルピー衝撃試験片の幅 L Charpy impact test piece length H Charpy impact test piece thickness Width of W Charpy impact test piece
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｃ 38/54 Ｃ２２Ｃ 38/54 (72)発明者 古君 修 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 Ｆターム(参考） 4K032 AA01 AA02 AA04 AA08 AA09 AA10 AA13 AA14 AA15 AA16 AA19 AA20 AA21 AA22 AA24 AA27 AA29 AA31 AA33 AA35 AA36 AA37 AA39 BA01 CA02 CA03 CC02 CC03 CL03 4K037 EA01 EA02 EA04 EA05 EA09 EA10 EA12 EA13 EA14 EA15 EA17 EA18 EA19 EA20 EA23 EA25 EA27 EA29 EA31 EA32 EA33 EA35 EB07 EB08 EB09 EC01 FA02 FA03 FF02 FH01 FJ04 FJ05 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 7 Identification code FI theme code (reference) C22C 38/54 C22C 38/54 (72) Inventor Osamu Furukun 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Kawasaki F-Term in the Technical Research Laboratory of Steel Manufacturing Co., Ltd. EA13 EA14 EA15 EA17 EA18 EA19 EA20 EA23 EA25 EA27 EA29 EA31 EA32 EA33 EA35 EB07 EB08 EB09 EC01 FA02 FA03 FF02 FH01 FJ04 FJ05
Claims (15)
つ下記（１）〜（４）式を満足することを特徴とするマ
ルテンサイト系ステンレス鋼板。 15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕≦20.0％・・・（１） 〔Ｃ〕＋〔Ｎ〕＜0.030 ％ ・・・（２） 〔Ni〕＋0.5 ×（〔Mn〕＋〔Mo〕）＋30×〔Ｃ〕＞3.0 ・・・（３） 8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕 ＋４×〔Ni〕＋〔Mo〕≦18.0％・・・（４）1. In mass%, C: less than 0.02%, Si: 1.0% or less, Mn: less than 1.5%, P: 0.04% or less, S: 0.01% or less, Al: 0.1% or less, Ni: 1.5% or more. , Less than 4.0%, Cr: 11% or more, less than 15%, Mo: 0.5% or more, less than 2.0%, N: less than 0.02%, the balance consisting of Fe and unavoidable impurities, and (1) ~ A martensitic stainless steel sheet which satisfies the formula (4). 15.0% ≤ [Cr] + 1.5 x [Mo] + 1.2 x [Ni] ≤ 20.0% ... (1) [C] + [N] <0.030% ... (2) [Ni] + 0. 5 x ([Mn] + [Mo]) + 30 x [C]> 3.0 (3) 8.0% ≤ 72 x [C] + 40 x [N] + 3 x [Si] + 2 x [Mn] + 4 x [ Ni] + [Mo] ≤ 18.0% (4)
Cu：2.0 ％以下、Co：2.0 ％以下添加され、残部がFeお
よび不可避的不純物からなり、かつ下記（２）、（５）
〜（７）式を満足することを特徴とするマルテンサイト
系ステンレス鋼。 〔Ｃ〕＋〔Ｎ〕＜0.030 ％ ・・・（２） 15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕＋0.5 ×〔Cu〕 ＋0.3 ×〔Co〕≦20.0％・・・（５） 〔Ni〕＋0.5 ×( 〔Mn〕＋〔Mo〕＋〔Cu〕）＋30×〔Ｃ〕＞3.0 ・・（６） 8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕 ＋４×〔Ni〕＋〔Mo〕＋〔Cu〕＋0.8 ×〔Co〕≦18.0％・・・（７）2. In mass%, C: less than 0.02%, Si: 1.0% or less, Mn: less than 1.5%, P: 0.04% or less, S: 0.01% or less, Al: 0.1% or less, Ni: 1.5% or more. , Less than 4.0%, Cr: 11% or more, less than 15%, Mo: 0.5% or more, less than 2.0%, N: less than 0.02%, and further, one or both of Cu and Co are contained.
Cu: 2.0% or less, Co: 2.0% or less, the balance consisting of Fe and inevitable impurities, and (2) and (5) below.
~ Martensitic stainless steel characterized by satisfying the formula (7). [C] + [N] <0.030% (2) 15.0% ≦ [Cr] + 1.5 × [Mo] + 1.2 × [Ni] + 0.5 × [Cu] + 0.3 × [Co] ≦ 20.0% ・ ・ ・ (5) [Ni] + 0.5 × ([Mn] + [Mo] + [Cu]) + 30 × [C]> 3.0 ・ ・ (6) 8.0% ≦ 72 × [C] +40 × [N] + 3 × [Si] + 2 × [Mn] + 4 × [Ni] + [Mo] + [Cu] + 0.8 × [Co] ≦ 18.0% (7)
Ti、Nb、Ｖ、Zr、Taのうちから選ばれる１種または２種
以上がTi：0.2 ％以下、Nb：0.2 ％以下、Ｖ：0.2 ％以
下、Zr：0.2 ％以下、Ta：0.2％以下添加されてなるこ
とを特徴とするマルテンサイト系ステンレス鋼板。3. The steel sheet according to claim 1 or 2, further comprising:
One or more selected from Ti, Nb, V, Zr and Ta are Ti: 0.2% or less, Nb: 0.2% or less, V: 0.2% or less, Zr: 0.2% or less, Ta: 0.2% or less. A martensitic stainless steel sheet characterized by being added.
にさらに、Ｂ、Caの一方または両方がＢ：0.005 ％以
下、Ca：0.005 ％以下添加されてなることを特徴とする
マルテンサイト系ステンレス鋼板。4. Martensite, characterized in that one or both of B and Ca are added to the steel sheet according to any one of claims 1 to 3 in an amount of B: 0.005% or less and Ca: 0.005% or less. Series stainless steel plate.
にさらに、Ｗ、Mgの一方または両方がＷ：0.1 ％以下、
Mg：0.01％以下添加されてなることを特徴とするマルテ
ンサイト系ステンレス鋼板。5. The steel sheet according to claim 1, further comprising one or both of W and Mg, W: 0.1% or less,
Mg: A martensitic stainless steel sheet characterized by being added by 0.01% or less.
の引張強度が600MPa超え、900MPa未満であることを特徴
とする熱延マルテンサイト系ステンレス鋼板。6. A hot-rolled martensitic stainless steel sheet, wherein the steel sheet according to claim 1 has a tensile strength of more than 600 MPa and less than 900 MPa.
の引張強度が600MPa超え、900MPa未満であることを特徴
とする冷延マルテンサイト系ステンレス鋼板。7. A cold-rolled martensitic stainless steel sheet, wherein the steel sheet according to claim 1 has a tensile strength of more than 600 MPa and less than 900 MPa.
ト系ステンレス鋼板を車両構造用材料に使用することを
特徴とするマルテンサイト系ステンレス鋼板の使用方
法。8. A method of using a martensitic stainless steel sheet, which comprises using the martensitic stainless steel sheet according to claim 6 or 7 as a vehicle structural material.
ト系ステンレス鋼板が、車両の構造部材に使用された車
両。9. A vehicle in which the martensitic stainless steel sheet according to claim 6 or 7 is used as a structural member of the vehicle.
つ下記の（１）〜（４）式を満足する鋼スラブを熱間圧
延し、必要に応じて、熱延板焼鈍と酸洗を行うことを特
徴とする熱延マルテンサイト系ステンレス鋼板の製造方
法。 15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕≦20.0％・・・（１） 〔Ｃ〕＋〔Ｎ〕＜0.030 ％ ・・・（２） 〔Ni〕＋0.5 ×（〔Mn〕＋〔Mo〕）＋30×〔Ｃ〕＞3.0 ・・・（３） 8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕 ＋４×〔Ni〕＋〔Mo〕≦18.0％・・・（４）10. The composition of the molten steel is% by mass, C: less than 0.02%, Si: 1.0% or less, Mn: less than 1.5%, P: 0.04% or less, S: 0.01% or less, Al: 0.1% or less, Ni: 1.5% or more, less than 4.0%, Cr: 11% or more, less than 15%, Mo: 0.5% or more, less than 2.0%, N: less than 0.02%, with the balance being Fe and inevitable impurities, and A method for producing a hot-rolled martensitic stainless steel sheet, which comprises hot-rolling a steel slab satisfying the following formulas (1) to (4) and, if necessary, performing hot-rolled sheet annealing and pickling. . 15.0% ≤ [Cr] + 1.5 x [Mo] + 1.2 x [Ni] ≤ 20.0% ... (1) [C] + [N] <0.030% ... (2) [Ni] + 0. 5 x ([Mn] + [Mo]) + 30 x [C]> 3.0 (3) 8.0% ≤ 72 x [C] + 40 x [N] + 3 x [Si] + 2 x [Mn] + 4 x [ Ni] + [Mo] ≤ 18.0% (4)
Cu：2.0 ％以下、Co：2.0 ％以下添加され、残部がFeお
よび不可避的不純物からなり、かつ下記の（２）、
（５）〜（７）式を満足する鋼スラブを熱間圧延し、必
要に応じて、熱延板焼鈍と酸洗を行うことを特徴とする
熱延マルテンサイト系ステンレス鋼板の製造方法。 〔Ｃ〕＋〔Ｎ〕＜0.030 ％ ・・・（２） 15.0％≦〔Cr〕＋1.5 ×〔Mo〕＋1.2 ×〔Ni〕＋0.5 ×〔Cu〕 ＋0.3 ×〔Co〕≦20.0％・・・（５） 〔Ni〕＋0.5 ×( 〔Mn〕＋〔Mo〕＋〔Cu〕）＋30×〔Ｃ〕＞3.0 ・・（６） 8.0 ％≦72×〔Ｃ〕＋40×〔Ｎ〕＋３×〔Si〕＋２×〔Mn〕 ＋４×〔Ni〕＋〔Mo〕＋〔Cu〕＋0.8 ×〔Co〕≦18.0％・・・（７）11. The composition of the molten steel is% by mass, C: less than 0.02%, Si: 1.0% or less, Mn: less than 1.5%, P: 0.04% or less, S: 0.01% or less, Al: 0.1% or less, Ni: 1.5% or more, less than 4.0%, Cr: 11% or more, less than 15%, Mo: 0.5% or more, less than 2.0%, N: less than 0.02%, In addition, one or both of Cu and Co are included.
Cu: 2.0% or less, Co: 2.0% or less are added, the balance consists of Fe and unavoidable impurities, and the following (2),
A method for producing a hot-rolled martensitic stainless steel sheet, comprising hot-rolling a steel slab satisfying the formulas (5) to (7) and, if necessary, performing hot-rolled sheet annealing and pickling. [C] + [N] <0.030% (2) 15.0% ≦ [Cr] + 1.5 × [Mo] + 1.2 × [Ni] + 0.5 × [Cu] + 0.3 × [Co] ≦ 20.0% ・ ・ ・ (5) [Ni] + 0.5 × ([Mn] + [Mo] + [Cu]) + 30 × [C]> 3.0 ・ ・ (6) 8.0% ≦ 72 × [C] +40 × [N] + 3 × [Si] + 2 × [Mn] + 4 × [Ni] + [Mo] + [Cu] + 0.8 × [Co] ≦ 18.0% (7)
Ti、Nb、Ｖ、Zr、Taのうちから選ばれる１種または２種
以上がTi：0.2 ％以下、Nb：0.2 ％以下、Ｖ：0.2 ％以
下、Zr：0.2 ％以下、Ta：0.2％以下添加されてなるこ
とを特徴とする熱延マルテンサイト系ステンレス鋼板の
製造方法。12. The molten steel according to claim 10 or 11, further comprising
One or more selected from Ti, Nb, V, Zr and Ta are Ti: 0.2% or less, Nb: 0.2% or less, V: 0.2% or less, Zr: 0.2% or less, Ta: 0.2% or less. A method for producing a hot-rolled martensitic stainless steel sheet, which is characterized by being added.
にさらに、Ｂ、Caの一方または両方がＢ：0.005 ％以
下、Ca：0.005 ％以下添加されてなることを特徴とする
熱延マルテンサイト系ステンレス鋼板の製造方法。13. A hot rolling method, characterized in that one or both of B and Ca are added to the molten steel according to any one of claims 10 to 12 in an amount of B: 0.005% or less and Ca: 0.005% or less. Manufacturing method of martensitic stainless steel sheet.
にさらに、Ｗ、Mgの一方または両方がＷ：0.1 ％以下、
Mg：0.01％以下添加されてなることを特徴とする熱延マ
ルテンサイト系ステンレス鋼板の製造方法。14. The molten steel according to claim 10, further comprising one or both of W and Mg, W: 0.1% or less,
Mg: 0.01% or less is added, The manufacturing method of the hot-rolled martensitic stainless steel sheet characterized by the above-mentioned.
マルテンサイト系ステンレス鋼板に、さらに、冷間圧
延、焼鈍および酸洗を行うことを特徴とする冷延マルテ
ンサイト系ステンレス鋼板の製造方法。15. A hot rolled martensitic stainless steel sheet according to claim 10, further comprising cold rolling, annealing and pickling. Production method.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100374608C (en) * | 2005-03-29 | 2008-03-12 | 山西太钢不锈钢股份有限公司 | High-strength anti-corrosion steel plate for rail vehicle and its making method |
| JP2010001568A (en) * | 2003-05-14 | 2010-01-07 | Jfe Steel Corp | High-strength stainless steel sheet and method for production thereof |
| CN105986193A (en) * | 2015-03-16 | 2016-10-05 | 斯凯孚公司 | Bearing steel |
| JP2016180143A (en) * | 2015-03-24 | 2016-10-13 | Ｊｆｅスチール株式会社 | Ferrite-martensite two-phase stainless steel and manufacturing method therefor |
-
2002
- 2002-11-29 JP JP2002347132A patent/JP4192576B2/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010001568A (en) * | 2003-05-14 | 2010-01-07 | Jfe Steel Corp | High-strength stainless steel sheet and method for production thereof |
| CN100374608C (en) * | 2005-03-29 | 2008-03-12 | 山西太钢不锈钢股份有限公司 | High-strength anti-corrosion steel plate for rail vehicle and its making method |
| CN105986193A (en) * | 2015-03-16 | 2016-10-05 | 斯凯孚公司 | Bearing steel |
| JP2016180143A (en) * | 2015-03-24 | 2016-10-13 | Ｊｆｅスチール株式会社 | Ferrite-martensite two-phase stainless steel and manufacturing method therefor |
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