JPH06299299A - High strength martensitic stainless steel excellent in rusting resistance and its production - Google Patents
High strength martensitic stainless steel excellent in rusting resistance and its productionInfo
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- JPH06299299A JPH06299299A JP8482993A JP8482993A JPH06299299A JP H06299299 A JPH06299299 A JP H06299299A JP 8482993 A JP8482993 A JP 8482993A JP 8482993 A JP8482993 A JP 8482993A JP H06299299 A JPH06299299 A JP H06299299A
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- Prior art keywords
- stainless steel
- martensitic stainless
- rust resistance
- strength
- formula
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は耐銹性を必要とする用途
に使用される高強度マルテンサイト系ステンレス鋼及び
その製造方法に関わり、更に詳しくは例えば耐銹性に優
れた高強度ばねに関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength martensitic stainless steel used for applications requiring rust resistance and a method for producing the same, and more particularly to a high-strength spring excellent in rust resistance. It is a thing.
【０００２】[0002]
【従来の技術】近年、耐銹性・靭性の観点から自動車を
はじめとする車両用ばね等の材料にＳＵＳ３０４，ＳＵ
Ｓ３０１，ＳＵＳ６３１等のオーステナイト系ステンレ
ス鋼が使用されるようになってきた。最近、この種のス
テンレス鋼製品には、軽量化ニーズから引張強さで約２
０００N/mm2 クラスの高強度が要求されるようになって
きた。一方、ばね成形を容易とするため、成形前の引張
強さが１２００N/mm2 以下が要求される。更に、ばね製
品の靭性として衝撃値で５０J/mm2 以上が要求される。2. Description of the Related Art In recent years, from the viewpoint of rust resistance and toughness, SUS304, SU has been used as a material for springs for vehicles such as automobiles.
Austenitic stainless steels such as S301 and SUS631 have come to be used. Recently, this type of stainless steel product has a tensile strength of about 2 due to the need for weight reduction.
High strength of 000N / mm 2 class has come to be required. On the other hand, in order to facilitate spring forming, the tensile strength before forming is required to be 1200 N / mm 2 or less. Further, the toughness of spring products is required to have an impact value of 50 J / mm 2 or more.
【０００３】この２０００N/mm2 クラスの引張強さを満
足するために、従来ＳＵＳ６３１系が使用されている。
しかし、ＳＵＳ６３１系は強度を高加工率での冷間加工
による加工硬化で付与しているため、最終製品（例えば
ばね）加工前の強度が引張強さで約１７００N/mm2 以上
の高強度である。このため、ばね加工での成形性が悪
く、又、製品の靭性が衝撃値で５０J/mm2 未満で、靭性
に劣る。又、ＳＵＳ４２０Ｊ２等の高炭素マルテンサイ
ト系ステンレス鋼が検討されているが、耐銹性・靭性が
低く、商品化されていない。In order to satisfy the tensile strength of this 2000 N / mm 2 class, the SUS631 system has been conventionally used.
However, since the SUS631 system imparts strength by work hardening by cold working at a high working rate, the strength before processing the final product (eg, spring) has a high tensile strength of about 1700 N / mm 2 or more. is there. For this reason, the formability in spring processing is poor, and the toughness of the product is less than 50 J / mm 2 in impact value, resulting in poor toughness. High-carbon martensitic stainless steels such as SUS420J2 have been investigated, but they have not been commercialized because they have low rust resistance and toughness.
【０００４】[0004]
【発明が解決しようとする課題】本発明は高耐銹性・高
強度のマルテンサイト系ステンレス鋼及び加工熱処理方
法を提供するものである。SUMMARY OF THE INVENTION The present invention provides a martensitic stainless steel having high rust resistance and high strength, and a thermomechanical treatment method.
【０００５】[0005]
【課題を解決するための手段】本発明は、マルテンサイ
ト系ステンレス鋼の成分を種々検討した結果、以下の知
見を得たことによる。重量％で、Ｃ：０．１３％〜０．
２０％、Ｓｉ：０．６％〜３．０％、Ｎｉ：１．０％〜
２．５％、Ｃｒ：１１．０％〜１７．０％、Ｍｏ：１．
３％〜３．５％、Ｎ：０．０６％〜０．１３％、Ｂ：
０．００１％〜０．０１０％を含有し、かつ１式で表さ
れるＤＩの値が０（％）未満、２式で表されるＭＩの値
が０（％）未満、３式で表されるＡＲＩの値が１６〜２
２（％）、残部が実質的にＦｅ及び不可避的不純物から
なる合金組成とすることにより耐銹性に優れた高強度マ
ルテンサイト系ステンレス鋼が得られることを見出し
た。The present invention is based on the following findings as a result of various studies on the components of martensitic stainless steel. % By weight, C: 0.13% to 0.
20%, Si: 0.6% to 3.0%, Ni: 1.0% to
2.5%, Cr: 11.0% to 17.0%, Mo: 1.
3% to 3.5%, N: 0.06% to 0.13%, B:
The content of 0.001% to 0.010%, and the value of DI represented by formula 1 is less than 0 (%), the value of MI represented by formula 2 is less than 0 (%), represented by formula 3. ARI value is 16-2
It has been found that a high-strength martensitic stainless steel excellent in rust resistance can be obtained by using an alloy composition of 2 (%) and the balance substantially consisting of Fe and unavoidable impurities.
【０００６】又、該材料を１０５０℃以上の温度から空
冷以上の冷却速度で焼入れ、続いて３００℃以下の低温
で焼鈍した場合、マルテンサイト系ステンレス鋼で引張
強さが２０００N/mm2 以上、靭性が衝撃値で５０J/mm2
以上で耐銹性がＳＵＳ３０４並になることを見出した。
更に、該材料を６００〜８００℃の軟化焼鈍をすること
で、引張強さが１２００N/mm2 以下となって加工性が向
上し、容易に冷間成形ができること、及び冷間成形後１
０５０℃以上の温度から空冷以上の冷却速度で焼入れ、
続いて３００℃以下の低温で焼鈍した場合、マルテンサ
イト系ステンレス鋼で引張強さが２０００N/mm2 以上、
靭性が衝撃値で５０J/mm2 以上で耐銹性がＳＵＳ３０４
並になることを見出した。Further, when the material is quenched from a temperature of 1050 ° C. or higher at a cooling rate of air cooling or higher and subsequently annealed at a low temperature of 300 ° C. or lower, the tensile strength of martensitic stainless steel is 2000 N / mm 2 or higher, The toughness is an impact value of 50 J / mm 2
From the above, it was found that the rust resistance is comparable to that of SUS304.
Further, by subjecting the material to soft annealing at 600 to 800 ° C., the tensile strength becomes 1200 N / mm 2 or less, the workability is improved, and cold forming can be easily performed.
Quenching from a temperature of 050 ° C or higher at a cooling rate of air cooling or higher,
When subsequently annealed at a low temperature of 300 ° C or less, the tensile strength of the martensitic stainless steel is 2000 N / mm 2 or more,
The toughness is 50 J / mm 2 or more at impact value and the rust resistance is SUS304.
I found that I would be in line.
【０００７】更に、該材料の熱間線材圧延を６００〜８
００℃の軟化焼鈍をし、続いて伸線加工し、続いて６０
０〜８００℃の軟化焼鈍をすることで、目的の線径で引
張強さが１２００N/mm2 以下となって加工性が向上し、
容易に冷間ばね成形ができること、及び冷間ばね成形
後、１０００℃以上の温度から空冷以上の冷却速度で焼
入れ、続いて３００℃以下の低温で焼戻した場合、マル
テンサイト系ステンレス鋼で引張強さが２０００N/mm2
以上、靭性が衝撃値で５０J/mm2 以上で耐銹性がＳＵＳ
３０４並のコイルばねを得られることを見出した。 ＤＩ＝0.76Ｃｒ＋ 1.1Ｍｏ＋ 1.1Ｓｉ−Ｎｉ−30Ｃ−18Ｎ−8.0 ……１式 ＭＩ＝Ｎｉ＋30Ｃ＋18Ｎ＋0.83Ｃｒ＋ 1.2Ｓｉ＋ 1.2Ｍｏ−26.0……２式 ＡＲＩ＝Ｃｒ＋ 2.4Ｍｏ ……３式Further, the hot wire rolling of the material is performed at 600 to 8
Softening annealing at 00 ° C, followed by wire drawing, then 60
By performing softening annealing at 0 to 800 ° C, the tensile strength at the target wire diameter becomes 1200 N / mm 2 or less and the workability improves,
Cold spring forming is easy, and after cold spring forming, when tempered from a temperature of 1000 ° C or higher at a cooling rate of air cooling or higher, and subsequently tempered at a low temperature of 300 ° C or lower, tensile strength of martensitic stainless steel is increased. 2,000 N / mm 2
Above, the toughness is 50 J / mm 2 or more at impact value and the rust resistance is SUS
It has been found that 304 coil springs can be obtained. DI = 0.76Cr + 1.1Mo + 1.1Si-Ni-30C-18N-8.0 ...... 1 formula MI = Ni + 30C + 18N + 0.83Cr + 1.2Si + 1.2Mo-26.0 …… 2 formula ARI = Cr + 2.4Mo …… 3 formula
【０００８】[0008]
【作用】以下に本発明の成分限定理由を述べる。ＤＩの
式は母材中のδフェライト量に対する各種元素の影響を
調査した結果得られたもので、δフェライト量に対し効
果のある元素とその影響度を示すものである。Ｃｒ，Ｍ
ｏ，Ｓｉ，Ｃ，Ｎ，Ｎｉが影響を与える。ＤＩの値が０
（％）を超えるとδフェライトが存在し、硬さ及び靭性
を低下させるばかりか、焼入れ時にδフェライト界面に
炭窒化物を析出させ、耐銹性を著しく低下させるため０
（％）未満に限定した。The reasons for limiting the components of the present invention will be described below. The formula of DI is obtained as a result of investigating the influence of various elements on the amount of δ-ferrite in the base material, and shows the element effective for the amount of δ-ferrite and its influence degree. Cr, M
o, Si, C, N, Ni have an effect. The value of DI is 0
If it exceeds (%), δ-ferrite is present, which not only lowers hardness and toughness, but also precipitates carbonitrides at the δ-ferrite interface during quenching, significantly lowering rust resistance.
Limited to less than (%).
【０００９】ＭＩの式は母材中のマルテンサイト組織量
に対する各種元素の影響を調査した結果得られたもの
で、マルテンサイト組織量に対し効果のある元素とその
影響度を示すものである。Ｃｒ，Ｍｏ，Ｓｉ，Ｃ，Ｎ，
Ｎｉが影響を与える。ＭＩの値が０（％）を超えると焼
入れ組織中にオーステナイト組織が散在し、引張強さが
２０００N/mm2 以下になるため０（％）未満に限定し
た。ＡＲＩの式は母材の耐銹性に対する各種元素の影響
を調査した結果得られたもので、耐銹性に対し効果のあ
る元素とその影響度を示すものである。耐銹性に対して
は、Ｃｒ，Ｍｏ及びδフェライトが最も影響を与える。
ＡＲＩは母材の耐銹性向上のために１６（％）以上とす
るが、２２（％）を超えると製造性を悪くするため上限
を２２（％）に限定した。The MI formula is obtained as a result of investigating the influence of various elements on the martensite structure amount in the base metal, and shows the element effective on the martensite structure amount and its influence degree. Cr, Mo, Si, C, N,
Ni has an effect. When the MI value exceeds 0 (%), the austenite structure is scattered in the quenched structure and the tensile strength becomes 2000 N / mm 2 or less, so the value was limited to less than 0 (%). The ARI formula is obtained as a result of investigating the influence of various elements on the rust resistance of the base material, and shows the element effective on the rust resistance and its influence degree. Cr, Mo and δ ferrite have the greatest influence on rust resistance.
The ARI is set to 16 (%) or more to improve the rust resistance of the base material, but if it exceeds 22 (%), the manufacturability is deteriorated, so the upper limit is set to 22 (%).
【００１０】Ｃはマルテンサイト系ステンレス鋼の焼入
れ・焼戻し後の引張強さを２０００N/mm2 以上を確保す
るために０．１３％以上添加する。しかし、０．２０％
を超えて添加すると粗大炭化物を析出させて耐銹性や加
工性を低下させるばかりか、靭性が低下することから、
上限を０．２０％に限定した。Ｓｉは脱酸のために必要
な元素であるばかりか、靭性を下げることなく引張強さ
及び耐へたり性を向上する有効な元素であるため、０．
６％以上添加する。しかし、３．０％を超えて添加して
もその効果は飽和するばかりか反対に靭性を低下させる
ため、上限を３．０％に限定した。C is added in an amount of 0.13% or more in order to secure a tensile strength of 2000 N / mm 2 or more after quenching and tempering of martensitic stainless steel. However, 0.20%
If it is added in excess of, coarse carbides will be precipitated and not only the rust resistance and workability will decrease, but also the toughness will decrease,
The upper limit was limited to 0.20%. Si is not only an element necessary for deoxidation but also an effective element for improving the tensile strength and the sag resistance without lowering the toughness.
Add 6% or more. However, even if added in excess of 3.0%, the effect is saturated and, conversely, the toughness decreases, so the upper limit was limited to 3.0%.
【００１１】Ｎｉはマルテンサイト組織の靭性を向上す
る有効な元素であるため、１．０％以上添加する。しか
し、２．５％を超えて添加してもその効果は飽和するし
経済的でない。又、３式のＭＩの値が増大して残留オー
ステナイト組織が存在し硬さを低下させるため上限を
２．５％に限定した。Ｃｒは耐銹性を向上する有効な元
素であるため、１１．０％以上添加する。しかし、１
７．０％を超えて添加すると２式のＤＩの値が過大とな
ってδフェライト組織が存在し、硬さ及び耐銹性を著し
く低下させるため上限を１６．０％に限定した。Since Ni is an effective element for improving the toughness of the martensitic structure, it is added in an amount of 1.0% or more. However, even if added over 2.5%, the effect is saturated and it is not economical. Further, the upper limit was limited to 2.5% because the MI value in Equation 3 increases and there is a retained austenite structure, which lowers the hardness. Cr is an effective element that improves rust resistance, so 11.0% or more is added. But 1
When added in excess of 7.0%, the value of DI in formula 2 becomes excessive and a δ ferrite structure exists, and the hardness and rust resistance are significantly reduced, so the upper limit was limited to 16.0%.
【００１２】Ｍｏは耐銹性を向上する有効な元素である
ため、１．３％以上添加する。しかし、３．５％を超え
て添加するとその効果は飽和するばかりか、２式のＤＩ
の値が過大となってδフェライト組織が存在し、硬さ及
び耐銹性を著しく低下させるため上限を３．５％に限定
した。Ｎは引張強さ及び耐銹性を向上する有効な元素で
あるため、０．０６％以上添加する。しかし、０．１３
％を超えて添加すると飽和して気泡を生じ、製造性を悪
くするため上限を０．１３％に限定した。Ｂは焼入硬さ
を向上する有効な元素であり、又、製造性の面から熱間
加工性を改善する元素であるために、０．００１％以上
添加する。しかし、０．０１０％を超えて添加するとボ
ライドが析出し耐銹性が劣化するため上限を０．０１０
％に限定した。Since Mo is an effective element for improving rust resistance, 1.3% or more is added. However, if added over 3.5%, not only the effect will be saturated, but also DI of formula 2
Is excessively large and a δ-ferrite structure is present, and the hardness and rust resistance are significantly reduced, so the upper limit was limited to 3.5%. N is an effective element that improves the tensile strength and rust resistance, so 0.06% or more is added. However, 0.13
If it is added in excess of%, it saturates to generate bubbles, which deteriorates manufacturability, so the upper limit was set to 0.13%. B is an effective element for improving the quenching hardness and is an element for improving the hot workability in terms of manufacturability, so 0.001% or more is added. However, if added in excess of 0.010%, boride precipitates and rust resistance deteriorates, so the upper limit is 0.010.
Limited to%.
【００１３】次に、請求項１記載の成分の発明鋼を製造
する方法の限定理由を述べる。該材料は焼入れにて強度
及び耐銹性を付与するが、焼入れ温度が１０５０℃以下
であると、Ｃｒ炭化物及びδフェライトが析出して耐銹
性が劣化するばかりか、固溶Ｃ量が減り焼入強度が得ら
れなくなるため、焼入温度を１０５０℃以上に限定し
た。又、冷却速度は空冷以上であると残留オーステナイ
トを生成して焼入れ強さが低下するばかりか、焼き割れ
を起こすため、空冷以上に限定した。Next, the reasons for limiting the method for producing the invention steel having the composition described in claim 1 will be described. The material imparts strength and rust resistance by quenching, but when the quenching temperature is 1050 ° C. or less, Cr carbide and δ ferrite are precipitated and the rust resistance is deteriorated, and the amount of solid solution C is reduced. Since quenching strength cannot be obtained, the quenching temperature was limited to 1050 ° C or higher. If the cooling rate is higher than that of air cooling, retained austenite is generated, the quenching strength is lowered, and quench cracking occurs.
【００１４】該材料は焼入れ後、続いて焼戻しを施す
が、焼鈍温度が３００℃以上になると引張強さが２００
０N/mm2 以下となるため、焼鈍温度を３００℃以下に限
定した。該材料はマルテンサイト系ステンレス鋼である
ため、通常のマルテンサイト系ステンレス鋼の６００〜
８００℃の軟化焼鈍で、引張強さが１２００N/mm2 以下
として冷間ばね成形等、容易に冷間成形ができ、その後
の焼入れ・焼戻し処理で耐銹性、硬さ、靭性を付与する
ことができる。そのため、焼入れ・焼戻し処理前に冷間
成形性を確保するため６００〜８００℃の軟化焼鈍をす
ることにした。The material is tempered and then tempered, and has a tensile strength of 200 at an annealing temperature of 300 ° C. or higher.
Since it is 0 N / mm 2 or less, the annealing temperature is limited to 300 ° C. or less. Since the material is martensitic stainless steel, 600 to 60% of that of ordinary martensitic stainless steel is used.
With softening annealing at 800 ℃, tensile strength is 1200N / mm 2 or less, cold forming such as cold spring can be easily performed, and rust resistance, hardness and toughness are given by subsequent quenching and tempering. You can Therefore, it was decided to perform softening annealing at 600 to 800 ° C. in order to ensure cold formability before quenching and tempering.
【００１５】[0015]
【００１６】次に該材料でコイルばねを製造する場合、
目的の線径に熱間線材圧延後、軟化焼鈍を施した後で冷
間ばね成形を施すと生産性が悪い。従って、熱間線材圧
延材を６００〜８００℃で軟化焼鈍し、続いて目的の線
径に伸線加工を施し、続いて６００〜８００℃の軟化焼
鈍をし、目的の線径で引張強さが１２００N/mm2 以下と
した後、冷間ばね成形を施すことにした。Next, when a coil spring is manufactured from the material,
If hot wire is rolled to a target wire diameter, softening annealing is performed, and then cold spring forming is performed, productivity is poor. Therefore, the hot-rolled material is softened and annealed at 600 to 800 ° C, then drawn to the desired wire diameter, and then softened and annealed at 600 to 800 ° C to obtain the tensile strength at the desired wire diameter. Was set to 1200 N / mm 2 or less, and then cold spring forming was performed.
【００１７】[0017]
【実施例】表１に本発明の実施例を、表２に比較例を示
す。これらの実施例は、通常のステンレス鋼線の製造工
程で、溶製、熱間線材圧延し、７００℃で軟化焼鈍、伸
線加工減面率６０％、７００℃で軟化焼鈍を施してばね
成形前のステンレス素線とし、引張試験を行った。その
後、冷間コイルばね成形を施し、１１００℃焼入れ、２
５０℃で焼戻し処理を施して製品とした。その後、引張
試験、耐銹性、靭性の試験を行った。EXAMPLES Table 1 shows examples of the present invention, and Table 2 shows comparative examples. In these examples, in a normal stainless steel wire manufacturing process, melting, hot wire rod rolling, softening annealing at 700 ° C., wire drawing area reduction ratio 60%, softening annealing at 700 ° C. and spring forming. A tensile test was performed using the previous stainless steel strand. After that, cold coil spring forming is performed, quenching at 1100 ° C, 2
A product was obtained by tempering at 50 ° C. Then, a tensile test, a rust resistance, and a toughness test were conducted.
【００１８】[0018]
【表１】 [Table 1]
【００１９】[0019]
【表２】 [Table 2]
【００２０】[0020]
【表３】 [Table 3]
【００２１】[0021]
【表４】 [Table 4]
【００２２】No．１〜No．１７は本発明例である。No．
１８〜No．３０は比較例である。引張試験はＪＩＳ Ｚ
２２０１によりばね成形前のサイズφ７．５×３００mm
のステンレス素線に１１００℃焼入れ・２５０℃焼戻し
処理を施す前後で試験を行い、引張強さを測定した。本
発明例のばね成形前の素線の引張強さは１２００N/mm2
以下である。本発明例のコイルばね製品の引張強さは２
０００N/mm2 以上である。No. 1-No. Reference numeral 17 is an example of the present invention. No.
18-No. 30 is a comparative example. Tensile test is JIS Z
2201 size before spring formation φ7.5 × 300mm
The tensile strength was measured by performing a test before and after the 1100 ° C. quenching and 250 ° C. tempering treatment of the stainless steel wire of No. 1 above. In the example of the present invention, the tensile strength of the wire before spring forming is 1200 N / mm 2
It is the following. The tensile strength of the coil spring product of the present invention is 2
000 N / mm 2 or more.
【００２３】耐銹性評価試験はＪＩＳ Ｚ２３７１によ
り線材圧延後の線材を平板に熱間圧延、冷間圧延、１１
００℃焼入れ・２５０℃焼戻し処理を施し、表面研磨
後、１００×５０×１mmの板にて５００時間試験実施後
評価した。発明例の耐銹性ランクはＪＩＳ評点の９．５
以上である。靭性はＪＩＳ Ｚ２２０２によりばね成形
前の素線に１１００℃焼入れ・２５０℃焼戻し処理を施
した後、サイズφ７．５×５５mm、深さ１mmのＵノッチ
で室温で試験を行い、その時のシャルピー値にて評価し
た。本発明例の製品のシャルピー値は５０Ｊ／cm2 以上
であった。The rust resistance evaluation test is carried out according to JIS Z2371, and the wire rod after the wire rod is rolled into a flat plate is subjected to hot rolling, cold rolling, 11
After quenching at 00 ° C and tempering at 250 ° C and polishing the surface, evaluation was carried out after performing a test for 500 hours on a plate of 100 x 50 x 1 mm. The rust resistance rank of the invention example is 9.5 of JIS score.
That is all. For toughness, JIS Z2202 was used to subject strands before spring forming to 1100 ° C quenching and 250 ° C tempering, and then tested at room temperature with a U-notch of size φ7.5 x 55 mm and depth 1 mm. Evaluated. The Charpy value of the product of the present invention was 50 J / cm 2 or more.
【００２４】本発明例No．１〜No．３と比較例No．１
８，１９は１３．１Ｃｒ−１．２Ｓｉ−２．０Ｎｉ−
２．０Ｍｏ−０．１Ｎ−０．００４Ｂを基本成分として
Ｃ量（％）を変化させて引張強さ、靭性、耐銹性への影
響を調査したものである。比較例No．１８はＣ量（％）
が低いため製品の引張強さに劣っている。比較例No．１
９はＣ量（％）が高いため粗大炭化物が析出し、製品の
靭性、耐銹性に劣っている。本発明例No．２，４，５と
比較例No．２０，２１は１３．１Ｃｒ−２．０Ｎｉ−
２．０Ｍｏ−０．１６Ｃ−０．１Ｎ−０．００４Ｂを基
本成分としてＳｉ量（％）を変化させて引張強さ、靭
性、耐銹性への影響を調査したものである。比較例No．
２０はＳｉ量（％）が低いため製品の引張強さに劣って
いる。比較例No．２１はＳｉ量（％）が高いため製品の
靭性に劣っている。Inventive Example No. 1-No. 3 and Comparative Example No. 1
8 and 19 are 13.1Cr-1.2Si-2.0Ni-
The influence on tensile strength, toughness, and rust resistance was investigated by changing the C content (%) using 2.0Mo-0.1N-0.004B as a basic component. Comparative Example No. 18 is the amount of C (%)
It is inferior to the tensile strength of the product due to its low value. Comparative Example No. 1
Since No. 9 has a high C content (%), coarse carbides are precipitated and the toughness and rust resistance of the product are poor. Inventive Example No. 2, 4, 5 and Comparative Example No. 20, 21 is 13.1Cr-2.0Ni-
The effect of tensile strength, toughness, and rust resistance was investigated by changing the Si content (%) using 2.0Mo-0.16C-0.1N-0.004B as a basic component. Comparative Example No.
No. 20 is inferior to the tensile strength of the product because the Si content (%) is low. Comparative Example No. No. 21 has a high Si content (%) and thus is inferior in toughness of the product.
【００２５】本発明例No．６〜８と比較例No．２２，２
３は１３．１Ｃｒ−１．５Ｓｉ−２．０Ｍｏ−０．１８
Ｃ−０．０８Ｎ−０．００４Ｂを基本成分としてＮｉ量
（％）を変化させて引張強さ、靭性、耐銹性への影響を
調査したものである。比較例No．２２はＮｉ量（％）が
低いため製品の靭性に劣っている。比較例No．２３はＮ
ｉ量（％）が高いためＭＩの値が０以上になり残留オー
ステナイトが存在し、製品の引張強さに劣っている。Inventive Example No. 6 to 8 and Comparative Example No. 22, 2
3 is 13.1Cr-1.5Si-2.0Mo-0.18
C-0.08N-0.004B was used as a basic component, and the amount of Ni (%) was changed and the influence on tensile strength, toughness, and rust resistance was investigated. Comparative Example No. No. 22 has a low Ni content (%) and is inferior in toughness of the product. Comparative Example No. 23 is N
Since the i content (%) is high, the MI value becomes 0 or more, residual austenite is present, and the tensile strength of the product is poor.
【００２６】本発明例No．６，９，１０と比較例No．２
４，２５は２．０Ｎｉ−１．５Ｓｉ−０．１８Ｃ−０．
０８Ｎ−０．００４Ｂを基本成分としてＣｒ量（％）を
変化させて引張強さ、靭性、耐銹性への影響を調査した
ものである。比較例No．２４はＣｒ量（％）が低いため
ＡＲＩの値が低く耐銹性に劣っている。比較例No．２５
はＣｒ量（％）が高いためＤＩの値が０以上になりフェ
ライトが存在し、製品の引張強さ、靭性、耐銹性に劣っ
ている。本発明例No．１１〜１３と比較例No．２６，２
７は１４．０Ｃｒ−１．５Ｎｉ−１．１Ｓｉ−０．１６
Ｃ−０．１Ｎ−０．００４Ｂを基本成分としてＭｏ量
（％）を変化させて引張強さ、靭性、耐銹性への影響を
調査したものである。比較例No．２６はＭｏ量（％）が
低いためＡＲＩの値が低く耐銹性に劣っている。比較例
No．２７はＭｏ量（％）が高いためＤＩの値が０以上に
なりフェライトが存在し、製品の引張強さ、靭性、耐銹
性に劣っている。本発明例No．１１，１４，１５と比較
例No．２８は１４．０Ｃｒ−１．５Ｎｉ−１．１Ｓｉ−
２．０Ｍｏ−０．１６Ｃ−０．００４Ｂを基本成分とし
てＮ量（％）を変化させて引張強さ、靭性、耐銹性への
影響を調査したものである。比較例No．２８はＮ量
（％）が低いため製品の硬さに劣っている。Inventive Example No. 6, 9, 10 and Comparative Example No. Two
4, 25 are 2.0Ni-1.5Si-0.18C-0.
08N-0.004B was used as a basic component, and the amount of Cr (%) was changed to investigate the effects on tensile strength, toughness, and rust resistance. Comparative Example No. No. 24, which has a low Cr content (%), has a low ARI value and is inferior in rust resistance. Comparative Example No. 25
Since the Cr content (%) is high, the DI value becomes 0 or more and ferrite is present, and the product has poor tensile strength, toughness, and rust resistance. Inventive Example No. 11 to 13 and Comparative Example No. 26, 2
7 is 14.0Cr-1.5Ni-1.1Si-0.16.
The influence on tensile strength, toughness, and rust resistance was investigated by changing the amount of Mo (%) using C-0.1N-0.004B as a basic component. Comparative Example No. No. 26 has a low Mo content (%) and thus has a low ARI value and is inferior in rust resistance. Comparative example
No. In No. 27, since the Mo content (%) is high, the DI value becomes 0 or more and ferrite is present, and the tensile strength, toughness, and rust resistance of the product are inferior. Inventive Example No. 11, 14, 15 and Comparative Example No. 28 is 14.0Cr-1.5Ni-1.1Si-
The effect on tensile strength, toughness, and rust resistance was investigated by changing the N content (%) using 2.0Mo-0.16C-0.004B as a basic component. Comparative Example No. No. 28 has a low N content (%) and is inferior in hardness of the product.
【００２７】本発明例No．１１，１６，１７と比較例N
o．２９，３０は１４．０Ｃｒ−１．５Ｎｉ−１．１Ｓ
ｉ−２．０Ｍｏ−０．１６Ｃ−０．１Ｎを基本成分とし
てＢ量（％）を変化させて引張強さ、靭性、耐銹性への
影響を調査したものである。比較例No．２９はＢ量
（％）が低いため製品の引張強さ、靭性に劣っている。
比較例No．３０はＢ量（％）が高くボライドを生成する
ため製品の靭性、耐銹性に劣っている。Inventive Example No. 11, 16, 17 and Comparative Example N
o. 29 and 30 are 14.0Cr-1.5Ni-1.1S.
i-2.0Mo-0.16C-0.1N was used as a basic component and the B content (%) was changed to investigate the effects on tensile strength, toughness, and rust resistance. Comparative Example No. No. 29 has a low B content (%) and is inferior in tensile strength and toughness of the product.
Comparative Example No. No. 30, which has a high B content (%) and produces boride, is inferior in toughness and rust resistance of the product.
【００２８】以上の実施例から分かるように本発明鋼の
優位性が明らかである。As can be seen from the above examples, the superiority of the steel of the present invention is clear.
【００２９】[0029]
【発明の効果】本発明により耐銹性に優れた高強度ばね
等を提供することが可能で、産業上有効な効果がもたら
される。Industrial Applicability According to the present invention, it is possible to provide a high-strength spring or the like having excellent rust resistance, which brings about an industrially effective effect.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 村田 亘 光市大字島田3434番地 新日本製鐵株式会 社光製鐵所内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Wataru Murata 3434 Shimada, Omitsu-shi, Nippon Steel Co., Ltd.
Claims (5)
満、２式で表されるＭＩの値が０（％）未満、３式で表
されるＡＲＩの値が１６〜２２（％）で残部が実質的に
Ｆｅ及び不可避的不純物からなることを特徴とする耐銹
性に優れた高強度マルテンサイト系ステンレス鋼。 ＤＩ＝0.76Ｃｒ＋ 1.1Ｍｏ＋ 1.1Ｓｉ−Ｎｉ−30Ｃ−18Ｎ−8.0 ……１式 ＭＩ＝Ｎｉ＋30Ｃ＋18Ｎ＋0.83Ｃｒ＋ 1.2Ｓｉ＋ 1.2Ｍｏ−26.0……２式 ＡＲＩ＝Ｃｒ＋ 2.4Ｍｏ ……３式1. By weight%, C: 0.13% to 0.20%, Si: 0.6% to 3.0%, Ni: 1.0% to 2.5%, Cr: 11.0. % -17.0%, Mo: 1.3% -3.5%, N: 0.06% -0.13%, B: 0.001% -0.010%, and 1 formula The value of DI represented by 2 is less than 0 (%), the value of MI represented by 2 is less than 0 (%), the value of ARI represented by 3 is 16 to 22 (%), and the remainder is substantially. A high-strength martensitic stainless steel having excellent rust resistance, which is characterized by comprising Fe and inevitable impurities. DI = 0.76Cr + 1.1Mo + 1.1Si-Ni-30C-18N-8.0 ...... 1 formula MI = Ni + 30C + 18N + 0.83Cr + 1.2Si + 1.2Mo-26.0 …… 2 formula ARI = Cr + 2.4Mo …… 3 formula
レス鋼を１０５０℃以上の加熱温度で焼入れし、続いて
３００℃以下で焼戻しをすることを特徴とする耐銹性に
優れた高強度マルテンサイト系ステンレス鋼の製造方
法。2. A high-strength martensite having excellent rust resistance, which comprises quenching the martensitic stainless steel according to claim 1 at a heating temperature of 1050 ° C. or higher and subsequently tempering it at 300 ° C. or lower. Of producing stainless steel.
レス鋼を６００〜８００℃で軟化焼鈍し、続いて冷間成
形加工し、続いて１０５０℃以上の加熱温度で焼入れ
し、続いて３００℃以下で焼戻しをすることを特徴とす
る耐銹性に優れた高強度マルテンサイト系ステンレス鋼
の冷間加工品の製造方法。3. The martensitic stainless steel according to claim 1 is softened and annealed at 600 to 800 ° C., then cold-formed, then quenched at a heating temperature of 1050 ° C. or higher, and subsequently 300 ° C. or lower. A method for manufacturing a cold-worked product of high-strength martensitic stainless steel having excellent rust resistance, which is characterized by performing tempering at.
レス鋼の熱間線材圧延材を６００〜８００℃で軟化焼鈍
し、続いてばね成形加工し、続いて１０５０℃以上の加
熱温度で焼入れし、続いて３００℃以下で焼戻しをする
ことを特徴とする耐銹性に優れた高強度マルテンサイト
系ステンレス鋼のコイルばねの製造方法。4. The hot-rolled martensitic stainless steel wire rod according to claim 1 is softened and annealed at 600 to 800 ° C., subsequently spring-formed, and then quenched at a heating temperature of 1050 ° C. or higher, Then, a method for producing a coil spring of high-strength martensitic stainless steel having excellent rust resistance, which is characterized by tempering at 300 ° C. or lower.
レス鋼の熱間線材圧延材を６００〜８００℃で軟化焼鈍
し、続いて伸線加工を施し、続いて６００〜８００℃で
軟化焼鈍し、続いてばね成形加工し、続いて１０５０℃
以上の加熱温度で焼入れし、続いて３００℃以下で焼戻
しをすることを特徴とする耐銹性に優れた高強度マルテ
ンサイト系ステンレス鋼のコイルばねの製造方法。5. The hot-rolled martensitic stainless steel wire rod according to claim 1 is softened and annealed at 600 to 800 ° C., followed by wire drawing, and then softened and annealed at 600 to 800 ° C., Next, spring forming process, then 1050 ℃
A method for producing a coil spring of high-strength martensitic stainless steel having excellent rust resistance, comprising quenching at the above heating temperature and subsequent tempering at 300 ° C. or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8482993A JPH06299299A (en) | 1993-04-12 | 1993-04-12 | High strength martensitic stainless steel excellent in rusting resistance and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP8482993A JPH06299299A (en) | 1993-04-12 | 1993-04-12 | High strength martensitic stainless steel excellent in rusting resistance and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH06299299A true JPH06299299A (en) | 1994-10-25 |
Family
ID=13841665
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP8482993A Withdrawn JPH06299299A (en) | 1993-04-12 | 1993-04-12 | High strength martensitic stainless steel excellent in rusting resistance and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH06299299A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2371560A (en) * | 2000-12-15 | 2002-07-31 | Hitachi Metals Ltd | Wire for reinforcing glass |
| JP2003293095A (en) * | 2002-04-04 | 2003-10-15 | Walsin Lihwa Corp | High-strength martensitic stainless steel material |
| JP2007314815A (en) * | 2006-05-23 | 2007-12-06 | Nippon Steel & Sumikin Stainless Steel Corp | Thick-sized high strength martensitic stainless steel wire and wire rod having excellent spring cold formability and method for producing steel wire |
-
1993
- 1993-04-12 JP JP8482993A patent/JPH06299299A/en not_active Withdrawn
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB2371560A (en) * | 2000-12-15 | 2002-07-31 | Hitachi Metals Ltd | Wire for reinforcing glass |
| GB2371560B (en) * | 2000-12-15 | 2005-07-13 | Hitachi Metals Ltd | Wire for reinforcing glass, glass sealing the same and glass plate having stainless steel wire sealed |
| JP2003293095A (en) * | 2002-04-04 | 2003-10-15 | Walsin Lihwa Corp | High-strength martensitic stainless steel material |
| JP2007314815A (en) * | 2006-05-23 | 2007-12-06 | Nippon Steel & Sumikin Stainless Steel Corp | Thick-sized high strength martensitic stainless steel wire and wire rod having excellent spring cold formability and method for producing steel wire |
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