JP2537679B2 - High-strength stainless steel and its steel material - Google Patents
High-strength stainless steel and its steel materialInfo
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- JP2537679B2 JP2537679B2 JP1043236A JP4323689A JP2537679B2 JP 2537679 B2 JP2537679 B2 JP 2537679B2 JP 1043236 A JP1043236 A JP 1043236A JP 4323689 A JP4323689 A JP 4323689A JP 2537679 B2 JP2537679 B2 JP 2537679B2
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は高強度（高硬度）が要求される部材や部品例
えば各種薄板ばね、刃物、かみそり替刃、カッター芯材
などに好適なステンレス鋼およびその鋼材とその製造方
法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention relates to stainless steel suitable for members and parts requiring high strength (high hardness) such as various leaf springs, blades, razor blades, and cutter core materials. And a steel material thereof and a manufacturing method thereof.
従来、高強度が要求される部材や部品材料用高強度ス
テンレス鋼としてマルテンサイト系ステンレス鋼、加工
硬化型オーステナイト系ステンレス鋼あるいは析出硬化
型ステンレス鋼などが使用されている。Conventionally, martensitic stainless steel, work hardening type austenitic stainless steel, precipitation hardening type stainless steel, etc. have been used as high strength stainless steel for members and parts materials requiring high strength.
マルテンサイト系ステンレス鋼はSUS410、420J1、420
J2、440A,B,Cなどに代表されるもので、これらの鋼は焼
入れ焼もどしにより高強度が得らえるので刃物、かみそ
り替刃などの用途に使用されている。しかしながら、マ
ルテンサイト系ステンレス鋼の焼入れ処理は950〜1100
℃の高温域から冷却するものであり、冷却過程でマルテ
ンサイト変態により形状が損なわれやすく、これを防止
するためにはプレス・クエンチのような特殊熱処理を施
さなければならない。Martensitic stainless steel is SUS410, 420J1, 420
These steels are typified by J2, 440A, B, C, etc. These steels are used for blades, razor replacement blades, etc., because high strength can be obtained by quenching and tempering. However, the quenching treatment of martensitic stainless steel is 950-1100.
It is cooled from a high temperature range of ℃, and the shape is easily damaged by martensite transformation in the cooling process. To prevent this, special heat treatment such as press quench must be performed.
SUS304、SUS301に代表される加工硬化型オーステナイ
ト系ステンレス鋼は焼却後の冷間加工によるオーステナ
イト（γ）相の加工硬化と加工誘起マルテンサイト
（α′）相の生成により高強度化を図るものである。し
かしながら、これらの鋼は冷間加工に加えて時効処理を
施してもビッカース硬さHvが高々500〜550程度であり、
高強度化を図るにも限界がある。Work hardening type austenitic stainless steels represented by SUS304 and SUS301 are intended to have high strength by work hardening of austenite (γ) phase and formation of work induced martensite (α ') phase by cold working after incineration. is there. However, these steels have a Vickers hardness Hv of at most about 500 to 550 even after aging treatment in addition to cold working,
There is a limit to achieving high strength.
析出硬化型ステンレス鋼には析出硬化元素としてCuを
添加したSUS630、Alを添加したSUS631がある。SUS630は
固溶化処理後の時効処理により硬化させるものである
が、ビッカース硬さHvが高々500程度である。SUS631は
準安定型オーステナイト系ステンレス鋼であり冷間加工
と時効処理を組み合わせ高強度化を図るものであるが、
この鋼材でもビッカース硬さHvが550程度が限界であ
る。またSUS631はAlを多量に含有しているためアルミナ
系の非金属介在物を形成し靱性や延性が低下する場合も
ある。Precipitation hardening type stainless steel includes SUS630 to which Cu is added as a precipitation hardening element and SUS631 to which Al is added. Although SUS630 is hardened by aging treatment after solution treatment, it has a Vickers hardness Hv of about 500 at most. SUS631 is a metastable austenitic stainless steel that combines cold working and aging treatment to achieve high strength.
Even with this steel, the Vickers hardness Hv is limited to around 550. In addition, since SUS631 contains a large amount of Al, alumina-based nonmetallic inclusions may be formed and the toughness and ductility may be reduced.
このようにこれらの高強度ステンレス鋼で得られる強
度レベルは低く、より高強度を有するステンレス鋼材の
開発が望まれていた。Thus, the strength levels obtained with these high-strength stainless steels are low, and the development of stainless steel materials having higher strength has been desired.
本発明者らは高強度ステンレス鋼材を得るには準安定
オーステナイト系ステンレス鋼に冷間加工を施し、加工
誘起マルテンサイト（α′）相を多量に生成させ、これ
に適度の時効処理を行いひずみ時効と析出時効により高
強度化を図ることが最も有効であると考え、鋭意研究を
重ねた結果、Siはオーステナイト（γ）相の安定度を低
下させ冷間加工の際のα′相の生成を促進させることに
より高強度化に寄与し、また、高Si含有鋼にNb、Ti、Ｖ
などの添加元素を含有させることにより冷間加工後300
〜600℃の時効処理を施すとビッカース硬さHv650以上の
極めて大きい時効硬化能が発現し高強度化が図れること
を見出した。In order to obtain a high-strength stainless steel material, the present inventors cold-work metastable austenitic stainless steel to generate a large amount of work-induced martensite (α ') phase, and subject it to appropriate aging treatment to cause strain. We believe that it is most effective to increase the strength by aging and precipitation aging, and as a result of intensive studies, Si reduces the stability of the austenite (γ) phase and forms α'phase during cold working. Contributes to higher strength by promoting the addition of Nb, Ti, V
After cold working by including additional elements such as 300
It was found that the aging treatment at ~ 600 ° C gives an extremely large age hardening ability with a Vickers hardness of Hv650 or more, and can increase the strength.
本発明は、 重量％で、 C:0.15％以下、 Si:3.0超え〜7.0％ Mn:8.0％以下 Ni:8.0〜13.0％ Cr:12.0〜17.0％ N:0.10％以下 を含有し、さらに、 Nb:1.0％以下、Ti:1.0％以下、V:1.0％以下、Zr:1.0％
以下の１種または２種以上を含有し、残部がFeと不可避
的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0であることを特徴
とする高強度ステンレス鋼を提供する。The present invention contains C: 0.15% or less, Si: more than 3.0 to 7.0% Mn: 8.0% or less, Ni: 8.0 to 13.0% Cr: 12.0 to 17.0% N: 0.10% or less, and further Nb. : 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, the balance consisting of Fe and unavoidable impurities, and Ni equivalent = Ni (%) + 0.60 Mn (%) + 9.69 (C + N) (%) + 0.18Cr ( %) −0.11Si (%) 2 +0.60 (Nb + Ti + V + Zr) (%), the value of Ni equivalent is 8.0 to 14.0.
本発明はまた上記組成を有し、実質的にマルテンサイ
ト（α′）相よりなり、ビッカース硬さHv650以上を有
することを特徴とする高強度ステンレス鋼材を提供す
る。The present invention also provides a high-strength stainless steel material having the above composition, being substantially composed of a martensite (α ') phase and having a Vickers hardness of Hv650 or more.
本発明はまた上記鋼に30％以上の冷間圧延を施した後
300〜600℃の温度範囲内で時効処理を施すことを特徴と
する高強度ステンレス鋼材の製造方法を提供する。The present invention also relates to the above steel after cold rolling of 30% or more.
Provided is a method for producing a high-strength stainless steel material characterized by performing an aging treatment within a temperature range of 300 to 600 ° C.
本発明はまた、 重量％で、 C:0.15％以下、 Si:3.0超え〜7.0％ Mn:8.0％以下 Ni:8.0〜13.0％ Cr:12.0〜17.0％ N:0.10％以下 を含有し、さらに、 Nb:1.0％以下、Ti:1.0％以下、V:1.0％以下、Zr:1.0％
以下の１種または２種以上を含有し、かつ、 Mo:3.0％以下、Cu3.0％以下の１種または２種を含有
し、 残部がFeと不可避的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） ＋0.60Mo（％）＋Cu（％） で定義されるNi当量の値が8.0〜14.0であることを特徴
とする高強度ステンレス鋼材を提供する。The present invention also contains, by weight%, C: 0.15% or less, Si: over 3.0 to 7.0% Mn: 8.0% or less Ni: 8.0 to 13.0% Cr: 12.0 to 17.0% N: 0.10% or less, and further, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, and contains one or two of Mo: 3.0% or less and Cu3.0% or less, the balance being Fe and inevitable impurities, and Ni equivalent = Ni (%) + 0.60Mn (%) + 9.69 (C + N) (%) + 0.18Cr (%)-0.11Si (%) 2 + 0.60 (Nb + Ti + V + Zr) (%) + 0.60Mo (%) + Cu (% ) Ni equivalent value is defined as 8.0 to 14.0, and a high strength stainless steel material is provided.
本発明はまた上記組成を有し、実質的にマルテンサイ
ト（α′）相からなり、ビッカース硬さHv650以上を有
することを特徴とする高強度ステンレス鋼材を提供す
る。The present invention also provides a high-strength stainless steel material having the above composition, being substantially composed of a martensite (α ') phase and having a Vickers hardness of Hv650 or more.
本発明はまた上記鋼に30％以上の冷間圧延を施した後
300〜600℃の温度範囲内で時効処理を施すことを特徴と
する高強度ステンレス鋼材の製造方法を提供する。The present invention also relates to the above steel after cold rolling of 30% or more.
Provided is a method for producing a high-strength stainless steel material characterized by performing an aging treatment within a temperature range of 300 to 600 ° C.
次に、本発明鋼において鋼組成の限定理由を以下に説
明する。Next, the reasons for limiting the steel composition in the steel of the present invention will be described below.
C:Cはオーステナイト生成元素でδフェライト相の生成
の抑制に寄与する。また、Ｃは冷間加工で誘発されたマ
ルテンサイト（α′）相の強化に有効である。しかしな
がら、本発明鋼ではSi含有量が高くＣの固溶限が低いた
めＣ含有量を高くすると粒界にCr炭化物が析出し耐粒界
腐食や延性低下をもたらす。したがってＣは0.15％以下
とする。C: C is an austenite forming element and contributes to the suppression of the formation of the δ ferrite phase. Further, C is effective in strengthening the martensite (α ') phase induced by cold working. However, in the steel of the present invention, since the Si content is high and the solid solubility limit of C is low, when the C content is increased, Cr carbide is precipitated at the grain boundaries, resulting in intergranular corrosion resistance and reduction in ductility. Therefore, C is 0.15% or less.
Si:Siは本発明鋼の特徴である高強度を発現させるに必
須の元素である。すなわち、Siはγ相の安定度を低下さ
せ冷間加工時にα′相の生成を促進させるとともにα′
相の強化にも寄与する。さらに、時効処理を程すことに
より強度を著しく増大させる。これらの特性を十分に発
揮させるにはSiは3.0％を超える量が必要である。しか
しながら、多量に含有されると熱間加工性は劣化するた
め上限を7.0％とする。Si: Si is an essential element for developing the high strength that is a characteristic of the steel of the present invention. That is, Si reduces the stability of the γ phase, promotes the formation of the α ′ phase during cold working, and
It also contributes to strengthening the phase. Further, the strength is remarkably increased by subjecting it to an aging treatment. Si is required to exceed 3.0% in order to fully exhibit these characteristics. However, if contained in a large amount, the hot workability deteriorates, so the upper limit is made 7.0%.
Mn:MnはNiと同様にオーステナイト生成元素であり焼鈍
材のオーステナイト組織を得るのに必要な元素である。
しかしながら、MnはNi当量を増大させる元素であり多く
含有させると冷間圧延時の加工誘起マルテンサイト
（α′）相の生成が阻害される。以上を鑑みてMnは8.0
％以下とする。Mn: Mn is an austenite forming element like Ni and is an element necessary for obtaining an austenite structure of an annealed material.
However, Mn is an element that increases the Ni equivalent, and when it is contained in a large amount, the formation of a work-induced martensite (α ') phase during cold rolling is hindered. Considering the above, Mn is 8.0
% Or less.
Ni:Niはオーステナイト系ステンレス鋼の基本的成分で
強力なオーステナイト生成元素である。Siを多量に含有
する本発明鋼においてδフェライトの生成を抑制し、焼
鈍状態で安定したオーステナイト相を得るためには8.0
％以上の含有が必要である。しかしながら、多量に含有
するとNi当量が増大し冷間圧延時のα′相の生成を抑制
するため上限を13.％とする。Ni: Ni is a basic component of austenitic stainless steel and is a strong austenite forming element. In order to suppress the formation of δ ferrite in the steel of the present invention containing a large amount of Si and obtain a stable austenite phase in the annealed state, 8.0
% Or more is required. However, if contained in a large amount, the Ni equivalent increases and the formation of α'phase during cold rolling is suppressed, so the upper limit is made 13.%.
Cr:Crはステンレス鋼の基本成分であり良好な耐食性を
得るには12.0％以上の含有が必要である。しかし、Crは
強力なフェライト生成元素であり多量に含有させと多量
のδフェライトと生成し熱間加工性を阻害するとともに
多量のδフェライトは高強度化を阻害するため上限を1
7.0％とする。Cr: Cr is a basic component of stainless steel, and 12.0% or more is necessary to obtain good corrosion resistance. However, Cr is a strong ferrite forming element, and if it is contained in a large amount, it forms a large amount of δ ferrite, which impedes hot workability and a large amount of δ ferrite impairs strengthening, so the upper limit is 1
7.0%
N:NはＣと同様、冷間圧延により生成されるα′相の固
溶強化に寄与することが0.10％を超えるとブローホール
を生成するなど健全な鋼塊が得られなくなるためこれを
上限とする。N: N, like C, contributes to the solid solution strengthening of the α'phase produced by cold rolling, and if it exceeds 0.10%, it will not be possible to obtain a sound steel ingot such as the formation of blowholes. And
Nb、Ti、Ｖ、Zr: Nb、Ti、ＶおよびZrは冷間圧延後の時効処理により高
強度化を図るのに有効であり、基本組織をγ相として冷
間圧延にてできるだけ多量のα′相を得た後時効処理す
ることを主眼とする本発明において重要な成分である。
しかし、添加量が増えるとδフェライトが生成され熱間
加工性が劣化するためそれぞれの上限を1.0％とする。Nb, Ti, V, and Zr: Nb, Ti, V, and Zr are effective in increasing the strength by aging treatment after cold rolling, and the basic structure is γ phase, and as much α as possible in cold rolling is used. It is an important component in the present invention whose main purpose is to perform aging treatment after obtaining the'phase.
However, if the addition amount increases, δ ferrite is generated and the hot workability deteriorates, so the upper limit of each is made 1.0%.
Mo:Moは結晶粒を微細化しまた、固溶強化により高強度
化に寄与しかつ、耐食性の向上にも有効であるが多量に
含有させると多量のδフェライトを生成し熱間加工性が
低下するためその上限を3.0％とする。Mo: Mo contributes to higher strength by refining crystal grains and strengthening solid solution and is also effective for improving corrosion resistance, but if a large amount is included, a large amount of δ ferrite is generated and hot workability deteriorates. Therefore, the upper limit is 3.0%.
Cu:CuはNiと同様オースーテナイト生成元素でありγ相
の安定化に寄与する。また、CuはMoと同様耐食性の向上
に寄与する。しかしながら、多量に含有すると熱加工性
が低下するため上限を3.0％とする。Cu: Cu is an austenite forming element like Ni and contributes to the stabilization of the γ phase. Further, Cu contributes to the improvement of corrosion resistance like Mo. However, if contained in a large amount, the heat workability is deteriorated, so the upper limit is made 3.0%.
次にNi当量、冷間圧延率および時効処理について説明
する。Next, the Ni equivalent, the cold rolling ratio and the aging treatment will be described.
Ni当量： Ni当量はα′変態に対するγ安定度の指標であり、次
式に示す経験式で表わされる。Ni equivalent: Ni equivalent is an index of γ stability against α ′ transformation, and is expressed by the empirical formula shown below.
Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） ＋0.60Mo（％）＋Cu（％） Ni当量が低いほど冷間圧延によるα′相の生成量が増加
し高強度化が図れるが低過ぎると焼鈍状態で多量のマル
テンサイト相が生成し、実質的にγ相が得られないため
その下限を8.0とする。一方、Ni当量が増加するとγ安
定度が増加し冷間加工時のα′相の生成が抑制され高強
度化が図れなくなるためその上限を14.0とする。Ni equivalent = Ni (%) + 0.60Mn (%) + 9.69 (C + N) (%) + 0.18Cr (%) -0.11Si (%) 2 + 0.60 (Nb + Ti + V + Zr) (%) + 0.60Mo (%) The lower the equivalent of + Cu (%) Ni, the more the amount of α'phase produced by cold rolling increases and the higher strength can be achieved. Therefore, the lower limit is set to 8.0. On the other hand, if the Ni equivalent is increased, the γ stability is increased and the α ′ phase is suppressed from being generated during cold working, so that the strength cannot be increased, so the upper limit is set to 14.0.
冷間圧延率： 本発明鋼は冷間圧延により多量のα′相を生成させそ
の後の時効処理により高強度化を図るものである。この
効果を発揮させるのに必要な冷間圧延率はNi当量に依存
しNi当量が高いほど付与すべき冷間圧延率は高くなる。
前述のようにNi当量が8.0〜14.0の範囲では30％以上の
冷間圧延率が必要である。Cold rolling ratio: The steel of the present invention is intended to increase the strength by cold rolling to produce a large amount of α'phase and subsequent aging treatment. The cold rolling rate required to exert this effect depends on the Ni equivalent, and the higher the Ni equivalent, the higher the cold rolling rate to be imparted.
As described above, when the Ni equivalent is in the range of 8.0 to 14.0, a cold rolling rate of 30% or more is required.
時効処理： 本発明鋼は冷間圧延により多量のα′相を生成させた
後適度な時効処理を施すことにより高強度を得るもので
ある。300℃以下では時効硬化能が十分ではなく高強度
が得られない。また、600℃以上の温度になると前処理
の冷間圧延により付与した歪みが緩和されやはり高強度
が得られなくなる。したがって、冷間圧延後の適切な時
効処理温度範囲を300〜600℃とする。なお、時効処理時
間は短時間でも十分であるが、安定した特性を得るには
30分以上の保持が必要である。Aging treatment: The steel of the present invention obtains a high strength by subjecting a large amount of α'phase to cold rolling to form an appropriate aging treatment. Below 300 ° C, the age hardening ability is not sufficient and high strength cannot be obtained. Further, at a temperature of 600 ° C. or higher, the strain imparted by the pre-treatment cold rolling is relaxed and high strength cannot be obtained. Therefore, the appropriate aging temperature range after cold rolling is 300 to 600 ° C. It should be noted that the aging treatment time is sufficient for a short time, but it is necessary to obtain stable characteristics.
Hold for 30 minutes or more.
（発明の具体的開示） 〔実施例〕 本発明鋼の特徴を従来鋼および比較鋼と比べて実施例
をもって明らかにする。(Specific Disclosure of the Invention) [Examples] The characteristics of the steel of the present invention will be clarified by Examples as compared with conventional steels and comparative steels.
第１表に本発明鋼、従来鋼および比較鋼の組成を示す。
試料No.1〜12鋼は本発明鋼であり、試料No.13、14は従
来鋼であり、各々SUS301鋼およびSUS631鋼である。また
試料No.15、16は比較鋼で試料No.15鋼はNi当量が本発明
の範囲内であるがSi含有量が本発明範囲を外れたもの、
試料No.16鋼は各成分元素含有量が本発明範囲内である
がNi当量が本発明範囲を外れたものである。各鋼を真空
下で12kg溶製後、35t×110w×ｌに鍛造、30t×105w×ｌ
に皮削り、熱間圧延にて3.0tとし溶体化処理、冷間圧
延、焼鈍を施した後冷間圧延にて0.9tに仕上げた。さら
に、これらの冷延鋼板に475℃×1hの時効処理を施し
た。 Table 1 shows the compositions of the present invention steel, conventional steel and comparative steel.
Sample Nos. 1 to 12 are steels of the present invention, Samples Nos. 13 and 14 are conventional steels, SUS301 steel and SUS631 steel, respectively. In addition, sample No. 15 and 16 are comparative steels and sample No. 15 steel has a Ni equivalent within the range of the present invention but a Si content outside the range of the present invention,
In the sample No. 16 steel, the content of each component element is within the range of the present invention, but the Ni equivalent is outside the range of the present invention. After melting 12kg of each steel under vacuum, forged to 35t × 110w × l, 30t × 105w × l
It was skinned, hot-rolled to 3.0 t, solution-treated, cold-rolled, annealed, and then cold-rolled to 0.9 t. Furthermore, these cold-rolled steel sheets were subjected to an aging treatment at 475 ° C for 1 hour.
第２表に各鋼の冷間圧延率、冷延後のマルテンサイト量
（α′量）、冷延のままと時効処理後の硬さ（Hv）、引
張強さ、延びおよび時効前後のビッカース硬さの差ΔHv
を示す。またあわせて本発明鋼の低冷間圧延材の比較例
を示す。本発明鋼である試料No.1〜12鋼は時効硬化能が
大きくΔHvが200以上あり時効処理後の硬さがHv650以上
である。これに対し従来鋼である試料No.13、14鋼、比
較鋼である試料No.15、16鋼および本発明鋼の30％未満
の冷延材では時効硬化能が低く時効処理後の硬さHvが65
0以下である。 Table 2 shows the cold rolling ratio of each steel, the amount of martensite (α ') after cold rolling, the hardness (Hv) after cold rolling and after aging, the tensile strength, the elongation and the Vickers before and after aging. Difference in hardness ΔHv
Indicates. In addition, a comparative example of the low cold rolled material of the present invention steel is also shown. The steels of the present invention, Sample Nos. 1 to 12, have large age hardening ability, ΔHv of 200 or more, and hardness after aging treatment of Hv650 or more. On the other hand, the conventional steel samples No. 13 and 14 steel, the comparative steel samples No. 15 and 16 steel, and the cold rolled steel of the present invention less than 30% have low age hardening ability and hardness after aging treatment. Hv is 65
It is 0 or less.
本発明は特定組成の高Si含有Cr−Ni系準安定オーステ
ナイト系ステンレス鋼およびそれに冷間圧延および時効
処理を施すことによりビッカース硬さHv650以上の著し
い高強度化を実現させたもので各種薄板ばね、刃物、替
刃、カッター芯材などに使用され得る高強度ステンレス
鋼ならびにその高強度ステンレス鋼材とその製造方法を
提供するものでその工業的価値は極めて高い。The present invention realizes a high Si content Cr-Ni metastable austenitic stainless steel of a specific composition and a significantly high strength of Vickers hardness Hv650 or more by subjecting it to cold rolling and aging treatment. The present invention provides high-strength stainless steel that can be used for blades, spare blades, cutter cores, and the like, as well as its high-strength stainless steel and its manufacturing method, and its industrial value is extremely high.
Claims (6)
以下の１種または２種以上を含有し、残部がFeと不可避
的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0であることを特徴
とする高強度ステンレス鋼。[Claim 1] C: 0.15% or less, Si: more than 3.0 to 7.0%, Mn: 8.0% or less, Ni: 8.0 to 13.0%, Cr: 12.0 to 17.0%, N: 0.10% or less. In addition, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, the balance consisting of Fe and unavoidable impurities, and Ni equivalent = Ni (%) + 0.60Mn (%) + 9.69 (C + N) (%) + 0.18Cr ( %) -0.11Si (%) 2 +0.60 (Nb + Ti + V + Zr) (%) A high-strength stainless steel having a Ni equivalent value of 8.0 to 14.0.
以下の１種または２種以上を含有し、残部がFeと不可避
的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0の範囲にある組成
を有し、実質的にマルテンサイト（α′）相からなり、
ビッカース硬さHv650以上を有することを特徴とする高
強度ステンレス鋼材。[Claim 2] C: 0.15% or less, Si: more than 3.0 to 7.0%, Mn: 8.0% or less, Ni: 8.0 to 13.0%, Cr: 12.0 to 17.0%, N: 0.10% or less in weight%. In addition, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, the balance consisting of Fe and unavoidable impurities, and Ni equivalent = Ni (%) + 0.60Mn (%) + 9.69 (C + N) (%) + 0.18Cr ( %) -0.11Si (%) 2 +0.60 (Nb + Ti + V + Zr) (%) has a composition in which the Ni equivalent value is in the range of 8.0 to 14.0, and is substantially composed of martensite (α ') phase. Becomes
A high-strength stainless steel material having a Vickers hardness of Hv650 or higher.
以下の１種または２種以上を含有し、残部がFeと不可避
的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0の範囲内にある鋼
に30％以上の冷間圧延を施した後300〜600℃の温度範囲
内に時効処理を施すことを特徴とする高強度ステンレス
鋼材の製造方法。3. In weight%, C: 0.15% or less, Si: more than 3.0 to 7.0%, Mn: 8.0% or less, Ni: 8.0 to 13.0%, Cr: 12.0 to 17.0%, N: 0.10% or less, In addition, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, the balance consisting of Fe and unavoidable impurities, and Ni equivalent = Ni (%) + 0.60 Mn (%) + 9.69 (C + N) (%) + 0.18Cr ( %) -0.11Si (%) 2 +0.60 (Nb + Ti + V + Zr) (%) Ni equivalent weight value within the range of 8.0 to 14.0 Steel after cold rolling of 30% or more 300 ~ A method for producing a high-strength stainless steel material, characterized by performing an aging treatment within a temperature range of 600 ° C.
以下の１種または２種以上を含有し、かつ、 Mo:3.0％以下、Cu3.0％以下の１種または２種を含有
し、残部がFeと不可避的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0であることを特徴
とする高強度ステンレス鋼。4. By weight%, C: 0.15% or less, Si: more than 3.0 to 7.0%, Mn: 8.0% or less, Ni: 8.0 to 13.0%, Cr: 12.0 to 17.0%, N: 0.10% or less, In addition, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, and contains one or two of Mo: 3.0% or less and Cu3.0% or less, the balance being Fe and inevitable impurities, and Ni equivalent = Ni (%) + 0.60 Mn (%) + 9.69 (C + N) (%) + 0.18Cr (%) -0.11Si (%) 2 + 0.60 (Nb + Ti + V + Zr) (%) High strength stainless steel characterized by being 8.0 to 14.0.
以下の１種または２種以上を含有し、かつ、 Mo:3.0％以下、Cu3.0％以下の１種または２種を含有
し、残部がFeと不可避的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0の範囲内にある組
成を有し、実質的にマルテンサイト（α′）相からな
り、ビッカース硬さHv650以上を有することを特徴とす
る高強度ステンレス鋼材。5. By weight%, C: 0.15% or less, Si: more than 3.0 to 7.0%, Mn: 8.0% or less, Ni: 8.0 to 13.0%, Cr: 12.0 to 17.0%, N: 0.10% or less, In addition, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, and contains one or two of Mo: 3.0% or less and Cu3.0% or less, the balance being Fe and inevitable impurities, and Ni equivalent = Ni (%) + 0.60 Mn (%) + 9.69 (C + N) (%) + 0.18Cr (%) -0.11Si (%) 2 + 0.60 (Nb + Ti + V + Zr) (%) A high-strength stainless steel material having a composition in the range of 8.0 to 14.0, being substantially composed of a martensite (α ') phase and having a Vickers hardness of Hv650 or more.
以下の１種または２種以上を含有し、かつ、 Mo:3.0％以下、Cu3.0％以下の１種または２種を含有
し、残部がFeと不可避的不純物からなり、かつ、 Ni当量＝Ni（％）＋0.60Mn（％） ＋9.69（Ｃ＋Ｎ）（％）＋0.18Cr（％） −0.11Si（％）２＋0.60（Nb＋Ti＋Ｖ＋Zr）（％） で定義されるNi当量の値が8.0〜14.0の範囲内にある鋼
に30％以上の冷間圧延を施した後300〜600℃の温度範囲
内に時効処理を施すことを特徴とする高強度ステンレス
鋼材の製造方法。6. By weight%, C: 0.15% or less, Si: 3.0 or more to 7.0%, Mn: 8.0% or less, Ni: 8.0 to 13.0%, Cr: 12.0 to 17.0%, N: 0.10% or less, In addition, Nb: 1.0% or less, Ti: 1.0% or less, V: 1.0% or less, Zr: 1.0%
Contains one or more of the following, and contains one or two of Mo: 3.0% or less and Cu3.0% or less, the balance being Fe and inevitable impurities, and Ni equivalent = Ni (%) + 0.60 Mn (%) + 9.69 (C + N) (%) + 0.18Cr (%) -0.11Si (%) 2 + 0.60 (Nb + Ti + V + Zr) (%) A method for producing a high-strength stainless steel material, which comprises subjecting steel in the range of 8.0 to 14.0 to cold rolling of 30% or more and then aging treatment in the temperature range of 300 to 600 ° C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1043236A JP2537679B2 (en) | 1989-02-27 | 1989-02-27 | High-strength stainless steel and its steel material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1043236A JP2537679B2 (en) | 1989-02-27 | 1989-02-27 | High-strength stainless steel and its steel material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02225646A JPH02225646A (en) | 1990-09-07 |
| JP2537679B2 true JP2537679B2 (en) | 1996-09-25 |
Family
ID=12658269
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1043236A Expired - Fee Related JP2537679B2 (en) | 1989-02-27 | 1989-02-27 | High-strength stainless steel and its steel material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2537679B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2803915B2 (en) * | 1991-02-27 | 1998-09-24 | 新日本製鐵株式会社 | Method of improving fatigue strength of high strength coil spring |
| JP3289947B2 (en) * | 1992-03-30 | 2002-06-10 | 日新製鋼株式会社 | Manufacturing method of stainless steel for high strength spring with excellent stress corrosion cracking resistance used in hot water environment |
| JP4841308B2 (en) * | 2006-05-12 | 2011-12-21 | 日新製鋼株式会社 | High-strength nonmagnetic stainless steel sheet and method for producing the same |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6179720A (en) * | 1984-09-27 | 1986-04-23 | Plus Eng Co Ltd | Printing wire for dot printer |
| JPH07103445B2 (en) * | 1986-04-30 | 1995-11-08 | 日新製鋼株式会社 | Blade stainless steel |
| JPH0826404B2 (en) * | 1987-06-22 | 1996-03-13 | 日新製鋼株式会社 | Method for producing high strength stainless steel with excellent overhang strength and toughness |
-
1989
- 1989-02-27 JP JP1043236A patent/JP2537679B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02225646A (en) | 1990-09-07 |
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