JPH09202944A - High strength stainless steel wire rope excellent in fatigue resistance and corrosion resistance and its production - Google Patents

Abstract

PROBLEM TO BE SOLVED: To produce a wire rope having respectively specified average crystalline grain size in cross-sectional direction and tensile strength by specifying the composition and manufacturing method of a stainless steel wire rope, respectively. SOLUTION: A wire rod, in as-hot-rolled state or after heat treatment, having a composition which consists of, by weight, <=0.12% C, 0.1-1.5% Si, >1.5-8.0% Mn, <=0.03% P, <=0.01% S, 3.5-7.5% Ni, 20.0-28.0% Cr, 0.1-3.0% Mo, and the balance Fe and in which the value of G1, represented by the equation, G1=0.67 Ni+20C+0.34Mn+0.4Cr+0.4Mo+0.6Si+3, is regulated to -1 to 2(%) is used. This wire rod is subjected to wire drawing at >=50% total reduction of area, to heat treatment at 1,000-1,150 deg.C, successively to wire drawing at 80-95% reduction of area, and then to stranding. By this method, the wire rope, having <=5μ average crystalline grain side in cross-sectional direction and >=1,500N/mm<2> tensile strength, can be obtained.

Description

【発明の詳細な説明】Detailed Description of the Invention

【０００１】[0001]

【発明の属する技術分野】本発明は耐疲労性、耐食性を
必要とする用途に使用される高強度ステンレス鋼ワイヤ
ロープ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 stainless steel wire rope used for applications requiring fatigue resistance and corrosion resistance.

【０００２】[0002]

【従来の技術】近年、メンテナンスフリーの観点から水
門用、エレベータ用等の高強度ワイヤロープの高耐食性
化の要求が高まってきた。すなわち、過酷な環境でも錆
びにくいようにＳＵＳ３０４並以上の耐食性が要求され
るようになってきた。また、この種の高強度ワイヤロー
プは長期間使用しても破損しないために高炭素鋼ロープ
と同等の耐疲労性が要求される。2. Description of the Related Art In recent years, there has been an increasing demand for high corrosion resistance of high strength wire ropes for sluices, elevators, etc. from the viewpoint of maintenance-free. That is, corrosion resistance equal to or higher than that of SUS304 has come to be required so as to prevent rusting even in a harsh environment. Further, this type of high-strength wire rope is not damaged even if it is used for a long period of time, and thus it is required to have fatigue resistance equivalent to that of a high carbon steel rope.

【０００３】従来、高強度のワイヤロープに高炭素鋼の
パーライト鋼が使用されてきた。しかし、耐食性が悪い
ばかりか、耐食性・耐疲労性のため表面に油を塗布して
おり、環境汚染も引き起こしてきた。そのため、高耐食
性の観点からＳＵＳ３０４，ＳＵＳ３１６等の伸線加工
されたオーステナイト系ステンレスワイヤロープの使用
が検討されてきた。しかし、オーステナト系ステンレス
ワイヤロープは長期間使用すると、繰り返し疲労による
早期破断が発生する問題があり、用途が制限されてい
る。Conventionally, high carbon steel pearlite steel has been used for high strength wire ropes. However, not only the corrosion resistance is poor, but oil is applied to the surface for corrosion resistance and fatigue resistance, which causes environmental pollution. Therefore, from the viewpoint of high corrosion resistance, the use of wire-drawn austenitic stainless wire rope such as SUS304 and SUS316 has been studied. However, when the austenato stainless steel wire rope is used for a long period of time, there is a problem that premature rupture occurs due to repeated fatigue, and its application is limited.

【０００４】一方、近年、２相ステンレス鋼の疲労強度
について、２相組織による結晶粒の微細化、２相組織の
硬質相の増加、２つの相の各相の耐力比の増大により耐
疲労性が向上することが提案されている（友田陽ら：鉄
と鋼，第６３号（１９７７），第６号，Ｐ６４）。ま
た、一般に鋼の高強度化により耐疲労性が向上されるこ
とが知られている（例えば、岡栄一ら：製鉄研究，第３
２０号（１９８６年），Ｐ２８）。さらに、伸線加工に
より高強度化された２相ステンレス鋼線の耐疲労性が伸
線加工により高強度化されたオーステナイト系ステンレ
ス鋼線より優れていることが確認されている（児玉勝
ら：ばね論文集，第３７号（１９９２年），Ｐ１）。On the other hand, in recent years, regarding the fatigue strength of duplex stainless steel, the fatigue resistance is increased by the refinement of crystal grains due to the two-phase structure, the increase of the hard phase of the two-phase structure, and the increase of the proof stress ratio of each phase of the two phases. Have been proposed (Yo Tomoda et al .: Iron and Steel, No. 63 (1977), No. 6, P64). Further, it is generally known that the fatigue resistance is improved by increasing the strength of steel (for example, Eiichi Oka et al .: Research on Steelmaking, No. 3
20 (1986), P28). Furthermore, it has been confirmed that the fatigue resistance of the duplex stainless steel wire strengthened by wire drawing is superior to the austenitic stainless steel wire strengthened by wire drawing (Kodama Katsu et al .: Spring Papers, No. 37 (1992), P1).

【０００５】そこで、最近、この２相ステンレス鋼の耐
疲労性に注目して、２相ステンレス鋼線の伸線材のワイ
ヤロープへの適用を提案している（特開平６−２８７７
１４号公報）。しかし、この２相ステンレス鋼ロープは
高炭素鋼ワイヤロープに対し、引張強さが低いという欠
点があり、耐疲労性を落とすこと無く、高強度化させる
ことが要求されている。すなわち、従来の２相ステンレ
ス鋼のレベルである１５００Ｎ／mm² 以上、好ましくは
高炭素鋼並以上の１７００Ｎ／mm² 以上が要求されてい
る。Therefore, recently, paying attention to the fatigue resistance of the duplex stainless steel, it has been proposed to apply the drawn wire of the duplex stainless steel wire to the wire rope (Japanese Patent Laid-Open No. 6-2877).
No. 14). However, this duplex stainless steel rope has a drawback that the tensile strength is low as compared with the high carbon steel wire rope, and it is required to increase the strength without lowering the fatigue resistance. That, 1500 N / mm ² or more at the level of a conventional two-phase stainless steel, preferably parallel over 1700 N / mm ² or more high-carbon steel is required.

【０００６】[0006]

【発明が解決しようとする課題】本発明は上記課題を解
決するものであり、耐疲労性、耐食性を必要とする用途
に使用される高強度ステンレス鋼ワイヤロープおよびそ
の製造方法を提供することを目的とする。SUMMARY OF THE INVENTION The present invention is to solve the above problems and provides a high strength stainless steel wire rope used for applications requiring fatigue resistance and corrosion resistance, and a method for producing the same. To aim.

【０００７】[0007]

【課題を解決するための手段】本発明は、２相ステンレ
ス鋼ワイヤロープの成分およびその製造方法を種々検討
した結果、以下の知見を得たことによる。すなわち、重
量％で、 (1) Ｃ ：０．１２％以下、 Ｓｉ：０．１％〜１．５％、 Ｍｎ：１．５％超〜８．０％、 Ｐ ：０．０３％以下、 Ｓ ：０．０１％以下、 Ｎｉ：３．５％〜７．５％、 Ｃｒ：２０．０％〜２８．０％、 Ｍｏ：０．１％〜３．０％ を含有し、下記式（１）で表されるＧ１の値が−１〜２
（％）で残部が実質的にＦｅおよび不可避的不純物から
なる合金組成で、横断面方向の平均結晶粒径が５μｍ以
下であり、引張強さが１５００Ｎ／mm² 以上にすると耐
疲労・耐食性に優れた高強度ステンレスワイヤロープが
得られることを見いだした。 Ｇ１＝０．６７Ｎｉ＋２０Ｃ＋０．３４Ｍｎ−０．４Ｃｒ−０．４Ｍｏ −０．６Ｓｉ＋３・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・（１）The present invention is based on the following findings as a result of various studies on components of a duplex stainless steel wire rope and a method for producing the same. That is, in% by weight, (1) C: 0.12% or less, Si: 0.1% to 1.5%, Mn: more than 1.5% to 8.0%, P: 0.03% or less, S: 0.01% or less, Ni: 3.5% to 7.5%, Cr: 20.0% to 28.0%, Mo: 0.1% to 3.0%, and the following formula ( The value of G1 represented by 1) is -1 to 2
(%) The balance is substantially Fe and unavoidable impurities, and the average crystal grain size in the transverse direction is 5 μm or less, and the tensile strength is 1500 N / mm ² or more, fatigue resistance and corrosion resistance are improved. It has been found that an excellent high-strength stainless wire rope can be obtained. G1 = 0.67Ni + 20C + 0.34Mn-0.4Cr-0.4Mo-0.6Si + 3 ...・ ・ ・ ・ ・ ・ ・ (1)

【０００８】(2) 上記(1) 記載の成分に、さらに重量％
で、 Ｎ ：０．１％〜０．３％ を含有し、下記式（２）で表されるＧ２の値が−１〜２
（％）であると、さらに、耐疲労、強度が向上すること
を見いだした。 Ｇ２＝０．６７Ｎｉ＋２０Ｃ＋２０Ｎ＋０．３４Ｍｎ−０．４Ｃｒ −０．４Ｍｏ−０．６Ｓｉ＋３・・・・・・・・・・・・・・・・・・・・・・・・・・・・（２）(2) In addition to the components described in (1) above, further weight%
And N: 0.1% to 0.3% is contained, and the value of G2 represented by the following formula (2) is -1 to 2
It has been found that when it is (%), fatigue resistance and strength are further improved. G2 = 0.67Ni + 20C + 20N + 0.34Mn-0.4Cr-0.4Mo-0.6Si + 3 ... (2)

【０００９】(3) 上記(1) 或いは(2) 記載の成分に、さ
らに重量％で、 Ｎｂ：０．０５％〜０．５０％、 Ｔｉ：０．０５％〜０．５０％ のうち１種または２種を含有し、下記式（３）で表され
るＧ３の値が−１〜２（％）で、鋼線の横断面方向の平
均結晶粒径が３μｍ未満であるとさらに、耐疲労性、強
度が向上することを見いだした。 Ｇ３＝０．６７Ｎｉ＋２０Ｃ＋２０Ｎ＋０．３４Ｍｎ−０．４Ｃｒ −０．４Ｍｏ−０．６Ｓｉ−０．９Ｔｉ−０．１Ｎｂ＋３・・・・（３）(3) In addition to the components described in (1) or (2) above, 1% of Nb: 0.05% to 0.50% and Ti: 0.05% to 0.50% by weight%. Or 2 kinds, the value of G3 represented by the following formula (3) is −1 to 2 (%), and the average grain size in the transverse direction of the steel wire is less than 3 μm, It has been found that fatigue strength and strength are improved. G3 = 0.67Ni + 20C + 20N + 0.34Mn-0.4Cr-0.4Mo-0.6Si-0.9Ti-0.1Nb + 3 ... (3)

【００１０】(4) 上記(1) ，(2) 或いは(3) 記載の成分
に、さらに重量％で、 Ａｌ：０．０１％以下、 Ｃａ：０．００１％〜０．００４％ を含有し、鋼線の横断面方向の介在物の大きさを２０μ
ｍ以下に抑制するとさらに、耐疲労性が向上することを
見いだした。(4) The composition described in (1), (2) or (3) above, further containing Al: 0.01% or less and Ca: 0.001% to 0.004% by weight. , The size of inclusions in the transverse direction of the steel wire is 20μ
It has been found that the fatigue resistance is further improved when the thickness is suppressed to m or less.

【００１１】(5) また、上記(1) ，(2) ，(3) 或いは
(4) 記載の成分を有する熱間線材圧延のまま或いは熱処
理後の線材を、減面率で５０％以上の伸線加工を施し、
その後、１０００℃〜１１５０℃の温度で熱処理後、引
き続き、減面率で８０％〜９５％の伸線加工を施し、そ
の後、ストランディングおよびクロージングの撚り線加
工を施すと耐疲労・耐食性に優れた高強度ステンレスワ
イヤロープが得られ、さらに、必要に応じて２００〜４
００℃の時効処理を施すと耐疲労性と強度がさらに向上
することを見いだした。(5) Further, the above (1), (2), (3) or
(4) Hot-rolled wire rods having the components described, or after being heat-treated, are subjected to wire drawing at a surface reduction rate of 50% or more,
After that, after heat treatment at a temperature of 1000 ° C to 1150 ° C, wire drawing work of 80% to 95% in area reduction is performed, and then stranding work of stranding and closing is performed, which is excellent in fatigue resistance and corrosion resistance. High-strength stainless wire rope can be obtained, and if necessary, 200-4
It has been found that fatigue resistance and strength are further improved by applying an aging treatment at 00 ° C.

【００１２】[0012]

【発明の実施の形態】本発明は、ワイヤロープの耐疲労
性、耐食性と高強度化の３特性を同時に満たすことを目
的とし、２相ステンレス鋼線の成分、伸線加工および熱
処理の最適化を行っている。すなわち、加工硬化、最適
な相分率、結晶粒微細化、各相の耐力比の増大を図って
いる。また、第３の硬質相を導入し、結晶粒微細化を促
進させ、高耐疲労性、高強度化を図り、さらに、介在物
の形態を抑制することで、耐疲労性の向上を図ってい
る。よって以下の条件に限定した。BEST MODE FOR CARRYING OUT THE INVENTION The present invention aims to simultaneously satisfy the three properties of wire rope: fatigue resistance, corrosion resistance and high strength, and optimizes the composition of duplex stainless steel wire, wire drawing and heat treatment. It is carried out. That is, work hardening, optimal phase fraction, grain refinement, and proof stress ratio of each phase are increased. In addition, by introducing a third hard phase to promote the refinement of crystal grains, to achieve high fatigue resistance and strength, and to suppress the form of inclusions, it is possible to improve fatigue resistance. There is. Therefore, the conditions are limited to the following.

【００１３】最初に、本発明の製造方法の限定理由を以
下に述べる。本発明は、請求項１〜４記載の成分の線材
に１回目の冷間伸線加工と熱処理を施し、その後、２回
目の冷間伸線加工を行い、鋼線の横断面方向の結晶粒を
微細化させるが、１回目の伸線加工で減面率が５０％未
満であると熱処理時の再結晶粒が粗大になり、最終製品
のワイヤロープの横断面方向の結晶粒が５μｍ超にな
る。この最終製品のワイヤロープの横断面方向の結晶粒
径と耐疲労性の関係を図１に示す。このワイヤロープは
０．０３Ｃ−０．４Ｓｉ−５．０Ｍｎ−６．５Ｎｉ−２
２．５Ｃｒ−１．２Ｍｏ−０．０３Ｎを基本成分とした
ステンレス鋼線材を１０〜８５％の減面率で伸線加工を
施し、続いて焼鈍炉にて１０５０℃の温度で５分間の連
続焼鈍を施し、その後、８５％の減面率で伸線加工を施
し、続いて、ストランディングおよびクロージングの撚
り線加工を施した。ワイヤロープ中の横断面方向の結晶
粒径が５μｍ超になると、耐疲労性であるＳ曲げ（Ｄ／
ｄ＝２０，ＳＦ＝６）での寿命までの回数が３００００
回未満となる。そのため、１回目の伸線加工での減面率
を５０％以上に限定した。First, the reasons for limiting the manufacturing method of the present invention will be described below. According to the present invention, the wire rod having the components according to claims 1 to 4 is subjected to the first cold drawing and heat treatment, and then the second cold drawing is performed to obtain crystal grains in the cross-sectional direction of the steel wire. However, if the area reduction rate is less than 50% in the first wire drawing, the recrystallized grains during the heat treatment will become coarse, and the grain size in the transverse direction of the wire rope of the final product will exceed 5 μm. Become. FIG. 1 shows the relationship between the grain size in the cross-sectional direction of the wire rope of this final product and the fatigue resistance. This wire rope is 0.03C-0.4Si-5.0Mn-6.5Ni-2.
A stainless steel wire rod whose basic component is 2.5Cr-1.2Mo-0.03N is subjected to wire drawing at a surface reduction rate of 10 to 85%, and then continuously in an annealing furnace at a temperature of 1050 ° C for 5 minutes. Annealing was performed, followed by wire drawing at an area reduction rate of 85%, followed by stranding and stranding for closing. If the crystal grain size in the cross-sectional direction in the wire rope exceeds 5 μm, the fatigue resistance S bending (D /
d = 20, SF = 6), the number of lifespan is 30000
Less than once. Therefore, the area reduction rate in the first wire drawing is limited to 50% or more.

【００１４】また、その後の熱処理で熱処理温度が１０
００℃未満であるとσ相が析出し、靭性を低下させ、伸
線性を悪くさせるばかりか、耐疲労性を低下させる。逆
に熱処理温度が１１５０℃超になると最終製品のワイヤ
ロープの横断面方向の結晶粒が粗大化し、５μｍ超にな
り、耐疲労性が劣化する。そのため、熱処理温度を１０
００℃以上、１１５０℃以下に限定した。In the subsequent heat treatment, the heat treatment temperature is 10
If the temperature is less than 00 ° C, the σ phase is precipitated, which lowers the toughness, deteriorates the wire drawability, and lowers the fatigue resistance. On the other hand, if the heat treatment temperature exceeds 1150 ° C., the crystal grains in the cross-sectional direction of the wire rope of the final product become coarse and become larger than 5 μm, and the fatigue resistance deteriorates. Therefore, the heat treatment temperature should be 10
The temperature was limited to 00 ° C or higher and 1150 ° C or lower.

【００１５】熱処理後、高強度化および高耐疲労性のた
め２回目の伸線加工を行う。この伸線加工での減面率と
ワイヤロープの強度の関係を図２に示す。このワイヤロ
ープは０．０３Ｃ−０．４Ｓｉ−５．０Ｍｎ−６．５Ｎ
ｉ−２２．５Ｃｒ−１．２Ｍｏ−０．０３Ｎを基本成分
としたステンレス鋼線材を６０％の減面率で伸線加工を
施し、続いて焼鈍炉にて１０５０℃の温度で５分間の連
続焼鈍を施した。その後、０〜９０％のトータル減面率
で伸線加工を施し、続いて、ストランディングおよびク
ロージングを行い、ワイヤロープを製作した。伸線加工
の減面率が８０％未満ではワイヤロープの引張強さが１
５００Ｎ／mm² 未満となる。そのため２回目の伸線加工
での減面率を８０％以上に限定した。After the heat treatment, a second wire drawing process is carried out in order to enhance strength and fatigue resistance. FIG. 2 shows the relationship between the area reduction rate in this wire drawing process and the strength of the wire rope. This wire rope is 0.03C-0.4Si-5.0Mn-6.5N
i-22.5Cr-1.2Mo-0.03N as a basic component, a stainless steel wire rod was subjected to wire drawing at a surface reduction rate of 60%, and then continuously in an annealing furnace at a temperature of 1050 ° C for 5 minutes. It was annealed. Then, wire drawing was performed at a total area reduction rate of 0 to 90%, followed by stranding and closing to manufacture a wire rope. If the reduction rate of wire drawing is less than 80%, the tensile strength of the wire rope is 1
It is less than 500 N / mm ² . Therefore, the area reduction rate in the second wire drawing is limited to 80% or more.

【００１６】しかし、伸線加工の減面率が９５％超にな
ると、図３に示すように伸線後の鋼線の引張破断絞りが
急激に低下し、靭性が劣化する。そのため、図４に示す
ようにワイヤロープの耐疲労性が３００００回未満と劣
化する。この図３，４の鋼線およびワイヤロープは０．
０３Ｃ−０．４Ｓｉ−５．０Ｍｎ−６．５Ｎｉ−２２．
５Ｃｒ−１．２Ｍｏ−０．０３Ｎを基本成分としたステ
ンレス鋼線材を６０％の減面率で伸線加工を施し、続い
て焼鈍炉にて１０５０℃の温度で５分間の連続焼鈍を施
した。その後、８０〜９９％の減面率で伸線加工を施
し、図４のワイヤロープは続いて、ストランディングお
よびクロージングの撚り線加工を施した。従って、２回
目の伸線加工率の上限を９５％に限定した。However, when the area reduction ratio of the wire drawing exceeds 95%, the tensile breaking reduction of the steel wire after wire drawing is drastically lowered as shown in FIG. 3, and the toughness is deteriorated. Therefore, as shown in FIG. 4, the fatigue resistance of the wire rope deteriorates to less than 30,000 cycles. The steel wire and wire rope of FIGS.
03C-0.4Si-5.0Mn-6.5Ni-22.
A stainless steel wire rod containing 5Cr-1.2Mo-0.03N as a basic component was subjected to wire drawing at a surface reduction rate of 60%, and then continuously annealed at a temperature of 1050 ° C for 5 minutes in an annealing furnace. . After that, wire drawing was performed at a surface reduction rate of 80 to 99%, and the wire rope of FIG. 4 was subsequently subjected to stranding of stranding and closing. Therefore, the upper limit of the second wire drawing rate is limited to 95%.

【００１７】さらに、その後、必要に応じて本発明の成
分系で時効処理を行う。本発明成分でのオーステナイト
相にはＭｎまたはＮが多く含有されているため、この時
効処理でオーステナイト相の高強度化によりオーステナ
イト相とフェライト相の耐力比の増大が起こり、耐疲労
性は急激に向上する。しかし、２００℃未満および４０
０℃超ではこの時効処理の効果が少ないため時効温度の
範囲を２００〜４００℃に限定した。After that, if necessary, an aging treatment is carried out with the component system of the present invention. Since the austenite phase in the component of the present invention contains a large amount of Mn or N, the aging treatment increases the strength of the austenite phase to increase the yield strength ratio of the austenite phase and the ferrite phase, and the fatigue resistance rapidly increases. improves. However, below 200 ° C and 40
If it exceeds 0 ° C, the effect of this aging treatment is small, so the range of aging temperature is limited to 200 to 400 ° C.

【００１８】次に、本発明の成分の限定理由を述べる。
Ｇ１，Ｇ２は本発明方法により各成分の２相ステンレス
鋼線材を６０％の減面率で伸線加工を施し、続いて焼鈍
炉にて１０５０℃の温度で５分間の連続焼鈍を施し、そ
の後、８５％の減面率で伸線加工を施し、続いて、スト
ランディングおよびクロージングの撚り線加工したワイ
ヤロープのオーステナイト相の量、引張強さおよび横断
面方向の平均結晶粒の関係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ある。Ｃ，Ｎ，Ｎｉ，Ｍｎ，
Ｃｒ，Ｓｉ，Ｍｏ，Ｎｂ，Ｔｉが影響を与える。Ｇ１，
Ｇ２の値が−１（％）未満であると、図５に示すように
ワイヤロープのオーステナイト相の量が４０％未満にな
り、図６に示すようにワイヤロープの製品の引張強度が
１５００Ｎ／mm² 未満になる。また、Ｇ１，Ｇ２の値が
２（％）超であると、図５に示すように、ワイヤロープ
中のオーステナイト相の量が７０％以上になり、単相組
織に近づくため結晶粒の粗大化がおこり、伸線加工後の
横断面方向の平均結晶粒を５μｍ以下にすることができ
ず、耐疲労性が低下する。そのため、Ｇ１，Ｇ２の値を
−１〜２（％）に限定した。Next, the reasons for limiting the components of the present invention will be described.
For G1 and G2, a duplex stainless steel wire rod of each component was drawn by a method of the present invention at a surface reduction rate of 60%, followed by continuous annealing at a temperature of 1050 ° C. for 5 minutes in an annealing furnace, and thereafter. , Various elements for the relationship between the amount of austenite phase, the tensile strength and the average grain size in the cross-sectional direction of the wire rope that has been subjected to wire drawing at a surface reduction rate of 85% and then stranding of stranding and closing It was obtained as a result of investigating the effect of. C, N, Ni, Mn,
Cr, Si, Mo, Nb and Ti have an influence. G1,
When the value of G2 is less than -1 (%), the amount of austenite phase of the wire rope becomes less than 40% as shown in FIG. 5, and the tensile strength of the wire rope product is 1500 N / as shown in FIG. less than mm ² . Further, when the values of G1 and G2 are more than 2 (%), the amount of austenite phase in the wire rope becomes 70% or more as shown in FIG. Occurs, the average grain size in the cross-sectional direction after wire drawing cannot be reduced to 5 μm or less, and the fatigue resistance decreases. Therefore, the values of G1 and G2 are limited to -1 to 2 (%).

【００１９】Ｃはワイヤロープの引張強さを確保、また
はオーステナイト相を得るため添加するが、０．１２％
を超えて添加すると粗大な粒界炭化物を生成し、耐食性
を劣化させるばかりか、耐疲労性も低下する。そのた
め、上限を０．１２％に限定した。Ｓｉは脱酸のために
必要な元素であるため、０．１％以上添加する。しか
し、１．５％を超えて添加してもその効果は飽和するば
かりか反対に靭性および耐疲労性を低下させるため、上
限を１．５％に限定した。C is added to secure the tensile strength of the wire rope or to obtain the austenite phase, but 0.12%
If it is added over the range, coarse grain boundary carbides are formed, which not only deteriorates the corrosion resistance but also reduces the fatigue resistance. Therefore, the upper limit is limited to 0.12%. Since Si is an element necessary for deoxidation, 0.1% or more is added. However, even if added in excess of 1.5%, the effect is saturated and, conversely, the toughness and fatigue resistance are reduced, so the upper limit was limited to 1.5%.

【００２０】Ｍｎは脱酸、鋼中のＳを固定するばかり
か、オーステナイト相の積層欠陥エネルギーを低下さ
せ、伸線加工による延性低下を抑えて高強度化を図るの
と、オーステナイト相とフェライト相の耐力比を増大さ
せ、耐疲労性を向上させるのに有効な元素であり、１．
５％超添加する。しかし、８．０％を超えて添加すると
Ｇ１，Ｇ２の値が大きくなり、オーステナイト相が７０
％超となり、耐疲労性が低下する。そのため、上限を
８．０％に限定した。Ｐは粒界偏析元素であり、ワイヤ
ロープの特性および製造性を悪くすることから０．０３
％以下に限定した。Mn not only deoxidizes and fixes S in steel, but also lowers the stacking fault energy of the austenite phase and suppresses the reduction of ductility due to wire drawing to enhance the strength, and the austenite and ferrite phases. Is an element effective in increasing the proof stress ratio and improving the fatigue resistance.
Add more than 5%. However, if the addition exceeds 8.0%, the values of G1 and G2 become large, and the austenite phase becomes 70%.
%, And fatigue resistance decreases. Therefore, the upper limit is limited to 8.0%. P is a grain boundary segregation element, which deteriorates the properties and manufacturability of the wire rope, so 0.03
% Or less.

【００２１】Ｓは粒界偏析元素であり、ワイヤロープの
特性および製造性を悪くすることから０．０１％以下に
限定した。Ｎｉはオーステナイト相を４０％以上得る有
効な元素であるため３．５％以上添加する。しかし、
７．５％を超えて添加するとＧ１，Ｇ２の値が大きくな
り、オーステナイト相が７０％超となり、耐疲労性が低
下する。そのため、上限を７．５％に限定した。S is a grain boundary segregating element, and is limited to 0.01% or less because it deteriorates the properties and manufacturability of the wire rope. Since Ni is an effective element for obtaining an austenite phase of 40% or more, Ni is added in an amount of 3.5% or more. But,
When added in excess of 7.5%, the values of G1 and G2 increase, the austenite phase exceeds 70%, and the fatigue resistance decreases. Therefore, the upper limit is limited to 7.5%.

【００２２】Ｃｒは耐銹性を向上し、フェライト相を得
る有効な元素であるため、２０．０％以上添加する。し
かし、２８．０％を超えて添加するとＧ１，Ｇ２の値が
小さくなり、オーステナイト相が４０％未満になり、耐
疲労性が低下する。そのため、上限を２８．０％にし
た。Ｍｏは耐食性を高め、また、強度を高めるのに有効
な元素であるため添加する。しかし、３．０％を超えて
添加してもその効果は飽和するし、Ｇ１，Ｇ２の値が小
さくなり、オーステナイト相が４０％未満になる。その
ため、上限を３．０％にした。Since Cr is an effective element for improving rust resistance and obtaining a ferrite phase, it is added in an amount of 20.0% or more. However, when added in excess of 28.0%, the values of G1 and G2 become small, the austenite phase becomes less than 40%, and the fatigue resistance decreases. Therefore, the upper limit is set to 28.0%. Mo is an element effective in enhancing the corrosion resistance and the strength, and is therefore added. However, even if added over 3.0%, the effect is saturated, the values of G1 and G2 become small, and the austenite phase becomes less than 40%. Therefore, the upper limit is set to 3.0%.

【００２３】Ｎは伸線加工時の延性低下を抑えて、高強
度を図るのと、オーステナイト相とフェライト相の耐力
比を増大させ耐疲労性を向上させるのに有効な元素であ
るため、必要によっては０．１０％以上を添加する。し
かし、０．３０％を超えて添加すると鋳造時にブローホ
ールが発生するばかりか、粒界の窒化物が発生し、耐疲
労性を低下させることから、上限を０．３０％に限定し
た。Ｎｂ，Ｔｉは第３の硬質相である炭窒化物の析出効
果により強度および耐疲労性を高めるのに有効な元素で
あるため、必要によっては０．０５％以上添加する。し
かし、添加し過ぎるとその効果は飽和するし、靭性を損
ない、耐疲労性を低下させる。そのため、上限をそれぞ
れ、０．５％に限定した。N is an element that is effective for suppressing the reduction of ductility during wire drawing, to achieve high strength, and for increasing the yield strength ratio of the austenite phase and the ferrite phase to improve fatigue resistance. Depending on the case, 0.10% or more is added. However, if added in excess of 0.30%, not only blowholes are generated during casting, but also nitrides at grain boundaries are generated and fatigue resistance is reduced, so the upper limit was limited to 0.30%. Nb and Ti are elements effective in increasing strength and fatigue resistance due to the precipitation effect of carbonitride, which is the third hard phase, and are therefore added in an amount of 0.05% or more as necessary. However, if added too much, the effect is saturated, the toughness is impaired, and the fatigue resistance is reduced. Therefore, the upper limits are limited to 0.5%.

【００２４】[0024]

【実施例】以下に本発明の実施例について説明する。表
１に試験した材料の成分を示す。また、表２、表３、表
４に実施例の製造条件および評価結果を示す。これらの
実施例は、通常のステンレス鋼線材の製造工程で、溶
製、熱間線材圧延した。その後、表２の実施例Ｎｏ．１
〜Ｎｏ．３２は、供試鋼Ａ〜Ｚ，ＡＡ〜ＡＦの各線材を
６０％の減面率で伸線加工を施し、続いて焼鈍炉にて１
０５０℃の温度で５分間の連続焼鈍を施した。その後、
８５％のトータル減面率で伸線加工を施し、続いて、ス
トランディンングおよびクロージングの撚り線加工を施
した。その後、ワイヤロープの特性として、横断面方向
の平均結晶粒径、オーステナイト相の比率、引張強さ、
耐疲労性、耐食性を評価し、成分の影響を調査した。Embodiments of the present invention will be described below. Table 1 shows the ingredients of the materials tested. Further, Table 2, Table 3, and Table 4 show the manufacturing conditions and evaluation results of the examples. In these examples, in a normal stainless steel wire manufacturing process, melting and hot wire rolling were performed. After that, the example Nos. 1
-No. In No. 32, wire rods of each of the test steels A to Z and AA to AF were subjected to wire drawing at a surface reduction rate of 60%, followed by 1 in an annealing furnace.
Continuous annealing was performed at a temperature of 050 ° C for 5 minutes. afterwards,
Wire drawing was performed at a total area reduction rate of 85%, followed by stranding and closing stranded wire processing. Then, as the characteristics of the wire rope, the average crystal grain size in the transverse direction, the ratio of the austenite phase, the tensile strength,
Fatigue resistance and corrosion resistance were evaluated and the influence of the components was investigated.

【００２５】また、表３、表４の実施例Ｎｏ．３３〜Ｎ
ｏ．４３は、供試鋼Ａの線材圧延材を３０〜８０％の減
面率で伸線加工を施し、続いて焼鈍炉にて９００℃〜１
２００℃の温度範囲で５分間の連続焼鈍を施した。その
後、減面率で６０％〜９８％の伸線加工を施し、ワイヤ
ロープにより線加工を行い、その後、必要に応じて５０
０℃以下で時効処理を行った。その後、ワイヤロープの
特性として、横断面方向の平均結晶粒径、オーステナイ
ト相の比率、引張強さ、耐疲労性を評価し、各工程の製
造条件の影響を調査した。In addition, the example Nos. In Tables 3 and 4 were used. 33 to N
o. In No. 43, the rolled wire rod of the sample steel A was subjected to wire drawing at a surface reduction rate of 30 to 80%, and then 900 ° C to 1 in an annealing furnace.
Continuous annealing was performed for 5 minutes in the temperature range of 200 ° C. After that, wire drawing is performed at a surface reduction rate of 60% to 98%, wire drawing is performed with a wire rope, and then 50% if necessary.
Aging treatment was performed at 0 ° C or lower. After that, as the characteristics of the wire rope, the average crystal grain size in the cross-sectional direction, the ratio of the austenite phase, the tensile strength, and the fatigue resistance were evaluated, and the influence of the manufacturing conditions in each step was investigated.

【００２６】横断面方向の結晶粒径およびオーステナイ
ト相の比率の測定は、最初にＪＩＳＧ０５７１によりエ
ッチを行い、続いて３０ｇのフェシリアン化カリウム、
３０ｇの水酸化カリウムと１００ｍｌの水の加熱した混
合液で浸漬エッチを行い、フェライト相に着色し、その
後、倍率が１０００倍で２０視野の平均粒径およびオー
ステナイト相の面積比率を画像解析により求めた。本発
明のワイヤロープの横断面方向の平均結晶粒径は５μｍ
以下であり、オーステナイト相の比率は４０〜７０％で
あった。The crystal grain size in the cross-sectional direction and the ratio of the austenite phase were measured by first performing etching according to JIS G 0571, and then using 30 g of potassium fesilianide,
Immersion etching was performed with a heated mixed solution of 30 g of potassium hydroxide and 100 ml of water to color the ferrite phase, and then the average grain size of 20 fields of view and the area ratio of the austenite phase were obtained by image analysis at a magnification of 1000 times. It was The average crystal grain size in the transverse direction of the wire rope of the present invention is 5 μm
The ratio of the austenite phase was 40 to 70%.

【００２７】引張試験はＪＩＳ Ｚ２２４１により製品
のワイヤロープの引張強さを測定した。本発明例のワイ
ヤロープの引張強さは１５００Ｎ／mm² 以上であった。
高炭素鋼ワイヤロープの引張強さは１７００Ｎ／mm² で
あった。In the tensile test, the tensile strength of the wire rope of the product was measured according to JIS Z2241. The tensile strength of the wire rope of the invention example was 1500 N / mm ² or more.
The tensile strength of the high carbon steel wire rope was 1700 N / mm ² .

【００２８】耐疲労性試験はＳ字曲げ疲労試験機を用
い、１ロープピッチ当たりの最外層素線の断線数が側ス
トランド構成総素線数の１０％に達したところで試験を
終了し、この時の繰り返し曲げ回数を耐疲労性の指標と
した。本発明例のワイヤロープの耐疲労性は高炭素鋼並
であった。For the fatigue resistance test, an S-shaped bending fatigue tester was used, and the test was terminated when the number of wire breaks in the outermost layer strand per rope pitch reached 10% of the total number of strands constituting the side strand. The number of repeated bendings was used as an index of fatigue resistance. The fatigue resistance of the wire rope of the example of the present invention was comparable to that of high carbon steel.

【００２９】耐食性は濃度が３％のＮａＣｌ溶液を３０
℃でワイヤロープに噴霧し、赤錆が発生するまでの時間
を測定した。但し、１０００ｈ試験しても赤錆が発生し
ないものについては１０００時間で試験を止めた。本発
明例のワイヤロープは８００時間以上でも錆びず、５２
０ｈ以上で赤錆が発生したＳＵＳ３０４以上であった。The corrosion resistance is 30% with a NaCl solution having a concentration of 3%.
The wire rope was sprayed at ℃, and the time until red rust was generated was measured. However, the test was stopped after 1000 hours for those in which red rust did not occur even after the 1000-hour test. The wire rope of the example of the present invention does not rust even after 800 hours,
It was SUS304 or more in which red rust was generated at 0 hours or more.

【００３０】最初に、ワイヤロープの特性として、横断
面方向の平均結晶粒径、オーステナイト相の比率、引張
強さ、耐疲労性、耐食性に及ぼす成分の影響を述べる。
Ｎｏ．１〜Ｎｏ．３は供試鋼Ａ〜Ｃの０．５Ｓｉ−３．
５Ｍｎ−６．５Ｎｉ−２２．５Ｃｒ−１．２Ｍｏ−０．
０２Ｎを基本成分としてオーステナイト生成元素である
Ｃ量（％）を変化させて、各元素の横断面方向の平均結
晶粒径、オーステナイト相の比率、引張強さ、耐疲労
性、耐食性への影響を調査し、本発明効果を確認したも
のである。供試鋼Ａ，Ｂにおいて本発明の効果が確認で
きる。比較例Ｎｏ．３はＣ量が高いため、耐疲労性に劣
る。First, as the characteristics of the wire rope, the effects of the components on the average crystal grain size in the transverse direction, the ratio of the austenite phase, the tensile strength, the fatigue resistance and the corrosion resistance will be described.
No. 1 to No. 3 is 0.5Si-3.
5Mn-6.5Ni-22.5Cr-1.2Mo-0.
By changing the amount of C (%) that is an austenite-forming element with 02N as a basic component, the effect on the average crystal grain size of each element in the cross-sectional direction, austenite phase ratio, tensile strength, fatigue resistance, corrosion resistance It was investigated and the effect of the present invention was confirmed. The effects of the present invention can be confirmed in the test steels A and B. Comparative Example No. Since No. 3 has a high C content, it is inferior in fatigue resistance.

【００３１】Ｎｏ．１，Ｎｏ．４〜Ｎｏ．７は供試鋼
Ａ，Ｄ〜Ｇの０．０３Ｃ−０．５Ｓｉ−６．５Ｍｎ−２
２．５Ｃｒ−１．２Ｍｏ−０．０２Ｎを基本成分として
オーステナイト生成元素であるＭｎ量（％）を変化させ
て、各元素の横断面方向の平均結晶粒径、オーステナイ
ト相の比率、引張強さ、耐疲労性、耐食性への影響を調
査し、本発明効果を確認したものである。供試鋼Ａ，
Ｅ，Ｆにおいて本発明の効果が確認できる。比較例Ｎ
ｏ．４はＭｎ量が低いため、引張強度に劣る。比較例Ｎ
ｏ．７はＭｎ量が高く、Ｇ１の値が高いため、オーステ
ナイト相の比率が高く、横断面方向の平均結晶粒径が大
きく、耐疲労性に劣る。No. 1, No. 4 to No. 7 is 0.03C-0.5Si-6.5Mn-2 of the sample steels A and D to G
2.5Cr-1.2Mo-0.02N is used as a basic component and the amount of Mn (%) that is an austenite-forming element is changed, and the average crystal grain size in the transverse direction of each element, the ratio of the austenite phase, and the tensile strength. The effects of the present invention were confirmed by investigating the effects on fatigue resistance and corrosion resistance. Test Steel A,
The effects of the present invention can be confirmed in E and F. Comparative Example N
o. Since No. 4 has a low Mn content, it has poor tensile strength. Comparative Example N
o. Since No. 7 has a high Mn content and a high G1 value, the ratio of the austenite phase is high, the average crystal grain size in the cross-sectional direction is large, and the fatigue resistance is poor.

【００３２】Ｎｏ．６，Ｎｏ．８，Ｎｏ．９は供試鋼
Ｆ，Ｈ，Ｉの０．０３Ｃ−７．０Ｍｎ−６．５Ｎｉ−２
２．２Ｃｒ−１．２Ｍｏ−０．０３Ｎを基本成分として
フェライト生成元素であるＳｉ量（％）を変化させて、
各元素の横断面方向の平均結晶粒径、オーステナイト相
の比率、引張強さ、耐疲労性、耐食性への影響を調査
し、本発明効果を確認したものである。供試鋼Ｆ，Ｈに
おいて本発明の効果が確認できる。比較例Ｎｏ．９はＳ
ｉ量が高いため、耐疲労性に劣る。No. 6, No. 8, No. 9 is 0.03C-7.0Mn-6.5Ni-2 of the sample steels F, H, and I.
2.2Cr-1.2Mo-0.03N is used as a basic component and the amount of Si (%) which is a ferrite forming element is changed,
The effects of the present invention were confirmed by investigating the influence of each element on the average crystal grain size in the cross-sectional direction, austenite phase ratio, tensile strength, fatigue resistance, and corrosion resistance. The effects of the present invention can be confirmed in the test steels F and H. Comparative Example No. 9 is S
Since the amount of i is high, the fatigue resistance is poor.

【００３３】Ｎｏ．１０〜Ｎｏ．１２は供試鋼Ｊ，Ｋ，
Ｌの０．０３Ｃ−０．５Ｓｉ−５．５Ｍｎ−２２．４Ｃ
ｒ−１．０Ｍｏ−０．０３Ｎを基本成分としてオーステ
ナイト生成元素であるＮｉ量（％）を変化させて、各元
素の横断面方向の平均結晶粒径、オーステナイト相の比
率、引張強さ、耐疲労性、耐食性への影響を調査し、本
発明効果を確認したものである。供試鋼Ｊにおいて本発
明の効果が確認できる。比較例Ｎｏ．１１はＮｉ量が低
いため、Ｇ１の値が低いため、オーステナイト相の比率
が低く、引張強さに劣るばかりか、横断面方向の平均結
晶粒径が大きく、耐疲労性に劣る。比較例Ｎｏ．１２は
Ｎｉ量が高く、Ｇ１の値が高いため、オーステナイト相
の比率が高く、横断面方向の平均結晶粒径が大きく、耐
疲労性に劣る。No. 10-No. 12 is the test steel J, K,
L 0.03C-0.5Si-5.5Mn-22.4C
By changing the amount (%) of Ni, which is an austenite-forming element, with r-1.0Mo-0.03N as a basic component, the average crystal grain size in the cross-sectional direction of each element, the ratio of the austenite phase, the tensile strength, and the resistance to The effect on the present invention was confirmed by investigating the effects on fatigue resistance and corrosion resistance. The effect of the present invention can be confirmed in the sample steel J. Comparative Example No. Since No. 11 has a low Ni content and a low G1 value, it has a low austenite phase ratio and is inferior in tensile strength, and also has a large average crystal grain size in the cross-sectional direction and is inferior in fatigue resistance. Comparative Example No. Since No. 12 has a high Ni content and a high G1 value, the ratio of the austenite phase is high, the average crystal grain size in the cross-sectional direction is large, and the fatigue resistance is poor.

【００３４】Ｎｏ．１３〜Ｎｏ．１６は供試鋼Ｍ〜Ｐの
０．０３Ｃ−０．５Ｓｉ−４．５Ｍｎ−７．１Ｎｉ−
１．０Ｍｏ−０．０３Ｎを基本成分としてフェライト生
成元素であるＣｒ量（％）を変化させて、各元素の横断
面方向の平均結晶粒径、オーステナイト相の比率、引張
強さ、耐疲労性、耐食性への影響を調査し、本発明効果
を確認したものである。供試鋼Ｍ，Ｎにおいて本発明の
効果が確認できる。比較例Ｎｏ．１５はＣｒ量が低く、
Ｇ１の値が高いため、オーステナイト相の比率が高く、
横断面方向の平均結晶粒径が大きく、耐疲労性に劣る。
比較例Ｎｏ．１６はＣｒ量が高く、Ｇ１の値が低いた
め、オーステナイト相の比率が低く、引張強さに劣る。No. 13-No. 16 is 0.03C-0.5Si-4.5Mn-7.1Ni- of the sample steels M to P.
The amount of Cr (%) that is a ferrite-forming element is changed with 1.0Mo-0.03N as a basic component, and the average grain size in the cross-sectional direction of each element, the ratio of the austenite phase, the tensile strength, and the fatigue resistance. The effect on the corrosion resistance was investigated and the effect of the present invention was confirmed. The effects of the present invention can be confirmed in the test steels M and N. Comparative Example No. 15 has a low Cr content,
Since the value of G1 is high, the ratio of the austenite phase is high,
The average grain size in the cross-sectional direction is large and the fatigue resistance is poor.
Comparative Example No. Since No. 16 has a high Cr content and a low G1 value, the ratio of the austenite phase is low and the tensile strength is poor.

【００３５】Ｎｏ．１７〜Ｎｏ．１９は供試鋼Ｑ〜Ｓの
０．０３Ｃ−０．５Ｓｉ−５．２Ｍｎ−６．４Ｎｉ−２
３Ｃｒ−０．０３Ｎを基本成分としてフェライト生成元
素であるＭｏ量（％）を変化させて、各元素の横断面方
向の平均結晶粒径、オーステナイト相の比率、引張強
さ、耐疲労性、耐食性への影響を調査し、本発明効果を
確認したものである。供試鋼Ｑ，Ｓにおいて本発明の効
果が確認できる。比較例Ｎｏ．１９はＭｏ量が高く、Ｇ
１の値が低いため、オーステナイト相の比率が低く、引
張強さに劣る。No. 17-No. 19 is 0.03C-0.5Si-5.2Mn-6.4Ni-2 of the sample steels QS.
3Cr-0.03N is used as a basic component and the amount of Mo (%), which is a ferrite-forming element, is changed, and the average crystal grain size in the cross-sectional direction of each element, austenite phase ratio, tensile strength, fatigue resistance, corrosion resistance The effect on the present invention was investigated and the effect of the present invention was confirmed. The effect of the present invention can be confirmed in the test steels Q and S. Comparative Example No. 19 has a high amount of Mo, G
Since the value of 1 is low, the ratio of the austenite phase is low and the tensile strength is poor.

【００３６】Ｎｏ．２０〜Ｎｏ．２３は供試鋼Ｔ〜Ｗの
０．０２Ｃ−０．５Ｓｉ−２．３Ｍｎ−２３Ｃｒ−１．
２Ｍｏを基本成分としてオーステナイト生成元素である
Ｎｉ量（％）とＮ量（％）を変化させて、各元素の横断
面方向の平均結晶粒径、オーステナイト相の比率、引張
強さ、耐疲労性、耐食性への影響を調査し、本発明効果
を確認したものである。供試鋼Ｔ，Ｕ，Ｖにおいて本発
明の効果が確認できる。特に、Ｎ量（％）を０．１０％
以上添加した供試鋼Ｕ，Ｖにおいては無添加の供試鋼Ｔ
より高強度・高耐疲労性を示し、本発明の効果が著し
い。比較例Ｎｏ．２３はＮ量が高いため、窒化物および
ブローホール生成のため、耐疲労性に劣る。No. 20-No. 23 is 0.02C-0.5Si-2.3Mn-23Cr-1.
By changing the amount of Ni (%) and the amount of N (%) that are austenite forming elements with 2Mo as a basic component, the average crystal grain size in the transverse direction of each element, austenite phase ratio, tensile strength, fatigue resistance The effect on the corrosion resistance was investigated and the effect of the present invention was confirmed. The effects of the present invention can be confirmed on the test steels T, U, and V. Especially, N amount (%) is 0.10%
In the test steels U and V added above, the test steel T without addition
It exhibits higher strength and fatigue resistance, and the effect of the present invention is remarkable. Comparative Example No. No. 23, which has a high N content, is inferior in fatigue resistance due to the formation of nitrides and blow holes.

【００３７】Ｎｏ．１，Ｎｏ．２４〜Ｎｏ．２５は供試
鋼Ａ，Ｘ，Ｙの０．０２Ｃ−０．５Ｓｉ−３．５Ｍｎ−
６．３Ｎｉ−２２．５Ｃｒ−０．０３Ｎを基本成分とし
て結晶粒微細化を促進させるＴｉ量（％）およびＮｂ量
（％）を変化させて、各元素の横断面方向の平均結晶粒
径、オーステナイト相の比率、引張強さ、耐疲労性、耐
食性への影響を調査し、本発明効果を確認したものであ
る。供試鋼Ａ，Ｘ，Ｙにおいて本発明の効果が確認でき
る。特にＴｉ量（％）を０．０５〜０．５％添加した供
試鋼Ｘと、Ｎｂ量（％）を０．０５〜０．５（％）添加
した供試鋼Ｙにおいては無添加の供試鋼Ａより高強度・
高耐疲労性を示し、本発明の効果が著しい。No. 1, No. 24-No. No. 25 is 0.02C-0.5Si-3.5Mn- of the sample steels A, X, and Y.
By changing the Ti amount (%) and the Nb amount (%) for promoting grain refinement with 6.3Ni-22.5Cr-0.03N as a basic component, the average crystal grain size of each element in the cross-sectional direction, The effects of the present invention were confirmed by investigating the effects on the ratio of austenite phase, tensile strength, fatigue resistance, and corrosion resistance. The effects of the present invention can be confirmed in the test steels A, X, and Y. In particular, in the test steel X added with 0.05 to 0.5% of Ti amount (%) and the test steel Y added with 0.05 to 0.5 (%) of Nb amount, no addition was made. Higher strength than test steel A
It exhibits high fatigue resistance and the effect of the present invention is remarkable.

【００３８】Ｎｏ．２１，Ｎｏ．２６〜Ｎｏ．３０は供
試鋼Ｕ，Ｚ，ＡＢ〜ＡＤの０．０２Ｃ−０．５Ｓｉ−
２．２Ｍｎ−４．８Ｎｉ−２２．８Ｃｒ−０．１５Ｎを
基本成分として結晶粒微細化を促進させるＴｉ量（％）
およびＮｂ量（％）を変化させて、各元素の横断面方向
の平均結晶粒径、オーステナイト相の比率、引張強さ、
耐疲労性、耐食性への影響を調査し、本発明効果を確認
したものである。供試鋼Ｕ，Ｚ〜ＡＢにおいて本発明の
効果が確認できる。特にＴｉ量（％）を０．０５〜０．
５％添加した供試鋼Ｚ，ＡＢと、Ｎｂ量（％）を０．０
５〜０．５（％）添加した供試鋼ＡＡ，ＡＢにおいては
無添加の供試鋼Ａより高強度・高耐疲労性を示し、本発
明の効果が著しい。比較例Ｎｏ．２９，３０はＴｉ量、
Ｎｂ量が高過ぎるため、耐疲労性に劣る。No. 21, No. 26-No. No. 30 is 0.02C-0.5Si- of the sample steels U, Z, AB to AD.
2.2 Mn-4.8Ni-22.8Cr-0.15N as a basic component to promote Ti grain refinement (%)
And the Nb amount (%) are changed to change the average crystal grain size in the transverse direction of each element, the ratio of the austenite phase, the tensile strength,
The effects on the present invention were confirmed by investigating the effects on fatigue resistance and corrosion resistance. The effects of the present invention can be confirmed in the sample steels U, Z to AB. Particularly, the Ti amount (%) is set to 0.05 to 0.
Steels Z and AB added with 5% and Nb content (%) of 0.0
The sample steels AA and AB added with 5 to 0.5 (%) exhibit higher strength and fatigue resistance than the sample steel A without addition, and the effect of the present invention is remarkable. Comparative Example No. 29 and 30 are Ti amount,
Since the amount of Nb is too high, the fatigue resistance is poor.

【００３９】Ｎｏ．２５，Ｎｏ．２８，Ｎｏ．３０〜Ｎ
ｏ．３４は供試鋼Ｙ，ＡＡ〜ＡＨの０．０２Ｃ−０．５
Ｓｉ−３．６Ｍｎ−６．７Ｎｉ−２２．６Ｃｒ−１．２
Ｍｏ−０．０３Ｎ（−０．４Ｎｂ）または０．０２Ｃ−
０．５Ｓｉ−２．３Ｍｎ−４．８Ｎｉ−２３Ｃｒ−０．
１５Ｎ（−０．３Ｎｂ）を基本成分として介在物のサイ
ズに影響を及ぼすＡｌ量（％）およびＣａ量（％）を変
化させて、横断面方向の平均結晶粒径、オーステナイト
相の比率、引張強さ、耐疲労性、耐食性への影響を調査
し、本発明効果を確認したものである。Ａｌ量（％）を
０．０１％以下に抑えて、Ｃａ量（％）を０．００２％
添加した供試鋼ＡＥ〜ＡＨにおいては無添加の供試鋼
Ｙ，ＡＡより高耐疲労性を示し、本発明の効果が著し
い。No. 25, no. 28, No. 30 to N
o. 34 is 0.02C-0.5 of the sample steels Y and AA to AH.
Si-3.6Mn-6.7Ni-22.6Cr-1.2
Mo-0.03N (-0.4Nb) or 0.02C-
0.5Si-2.3Mn-4.8Ni-23Cr-0.
By changing the Al amount (%) and Ca amount (%) that influence the size of inclusions with 15 N (-0.3 Nb) as a basic component, the average crystal grain size in the cross-sectional direction, austenite phase ratio, and tensile The effects on the present invention were confirmed by investigating the effects on strength, fatigue resistance and corrosion resistance. Al content (%) is suppressed to 0.01% or less, Ca content (%) is 0.002%
The added test steels AE to AH exhibit higher fatigue resistance than the non-added test steels Y and AA, and the effect of the present invention is remarkable.

【００４０】Ｎｏ．３５は供試鋼ＡＩのＳＵＳ３０４、
Ｎｏ．３６は供試鋼ＡＧの高炭素鋼のワイヤロープの特
性を評価したものである。ＳＵＳ３０４の比較例Ｎｏ．
３５は耐疲労性に劣り、高炭素鋼のワイヤロープの比較
例Ｎｏ．３６は耐食性に劣る。No. 35 is SUS304 of the test steel AI,
No. 36 is an evaluation of the characteristics of the wire rope of the high carbon steel of the test steel AG. Comparative example No. SUS304.
No. 35 is inferior in fatigue resistance, and is a high carbon steel wire rope comparative example No. 36 has poor corrosion resistance.

【００４１】次に、供試鋼Ａのワイヤロープの特性とし
て、横断面方向の平均結晶粒径、オーステナイト相の比
率、引張強さ、耐疲労性、耐食性に及ぼす各工程の製造
条件の影響を述べる。Ｎｏ．３７〜Ｎｏ．３９は１回目
の伸線加工率を３０％〜８０％まで変化させて、横断面
方向の平均結晶粒径、オーステナイト相とフェライト相
の比率、引張強さ、耐疲労性、耐食性への影響を調査
し、本発明効果を確認したものである。本発明例３８，
３９において本発明の効果が確認できる。比較例Ｎｏ．
３７は１回目の伸線加工率が低いため、その後の熱処理
で結晶粒径が十分に微細にならず、耐疲労性に劣る。Next, as the characteristics of the wire rope of the sample steel A, the influence of the manufacturing conditions of each step on the average grain size in the transverse direction, the ratio of the austenite phase, the tensile strength, the fatigue resistance, and the corrosion resistance was examined. Describe. No. 37-No. In No. 39, the first wire drawing ratio was changed from 30% to 80%, and the influence on the average crystal grain size in the transverse direction, the ratio of the austenite phase to the ferrite phase, the tensile strength, the fatigue resistance, and the corrosion resistance. It was investigated and the effect of the present invention was confirmed. Invention Example 38,
In 39, the effect of the present invention can be confirmed. Comparative Example No.
Since No. 37 has a low first wire drawing rate, the grain size is not sufficiently fined by the subsequent heat treatment and fatigue resistance is poor.

【００４２】Ｎｏ．３８，Ｎｏ．４０〜Ｎｏ．４３は熱
処理温度を９００℃〜１２００℃まで変化させて、横断
面方向の平均結晶粒径、オーステナイト相の比率、引張
強さ、耐疲労性、耐食性への影響を調査し、本発明効果
を確認したものである。本発明例３８，４１，４２にお
いて本発明の効果が確認できる。比較例Ｎｏ．４０は熱
処理温度が低いため、σ相が析出し、耐疲労性に劣る。
比較例Ｎｏ．４３は１回目の熱処理温度が高いため、オ
ーステナイト粒径が粗大化し、耐疲労性に劣る。No. 38, no. 40-No. In No. 43, the heat treatment temperature was changed from 900 ° C. to 1200 ° C., and the effect on the average crystal grain size in the transverse direction, the ratio of the austenite phase, the tensile strength, the fatigue resistance, and the corrosion resistance was investigated, and the effect of the present invention was confirmed. It was done. The effects of the present invention can be confirmed in Invention Examples 38, 41 and 42. Comparative Example No. Since No. 40 has a low heat treatment temperature, a σ phase precipitates and fatigue resistance is poor.
Comparative Example No. In No. 43, since the first heat treatment temperature is high, the austenite grain size becomes coarse and the fatigue resistance is poor.

【００４３】Ｎｏ．４４〜Ｎｏ．４８は２回目の伸線加
工率を６０％〜９８％まで変化させて、横断面方向の平
均結晶粒径、オーステナイト相の比率、引張強さ、耐疲
労性、耐食性への影響を調査し、本発明効果を確認した
ものである。本発明例Ｎｏ．４６，Ｎｏ．４７において
本発明の効果が確認できる。比較例Ｎｏ．４４，４５は
２回目の伸線加工率が低いため、引張強さに劣る。比較
例Ｎｏ．４８は２回目の伸線加工率が高いため、靭性の
低下により、耐疲労性に劣る。No. 44-No. No. 48 changes the second wire drawing rate from 60% to 98%, and investigates the influence on the average crystal grain size in the transverse direction, the ratio of the austenite phase, the tensile strength, the fatigue resistance, and the corrosion resistance, The effects of the present invention have been confirmed. Invention Example No. 46, no. 47, the effect of the present invention can be confirmed. Comparative Example No. Nos. 44 and 45 are low in tensile strength because the second wire drawing rate is low. Comparative Example No. Since No. 48 has a high second wire drawing rate, its toughness deteriorates, resulting in poor fatigue resistance.

【００４４】Ｎｏ．４９〜Ｎｏ．５３は２回目の伸線加
工後の時効処理温度を５００℃以下で変化させて、横断
面方向の平均結晶粒径、オーステナイト相の比率、引張
強さ、耐疲労性、耐食性への影響を調査し、本発明効果
を確認したものである。本発明例Ｎｏ．５０，５１，５
２において本発明の効果が著しく、引張強度が１７００
Ｎ／mm² を超えており、高炭素鋼並の強度と耐疲労性を
示す。本発明例Ｎｏ．４９は時効処理温度が低過ぎるた
め、強度および耐疲労性の向上が期待できない。本発明
例Ｎｏ．５３は時効処理温度が高過ぎるため、耐疲労性
の向上が期待できない。以上の実施例から分かるように
本発明例の優位性が明らかである。No. 49-No. In No. 53, the aging treatment temperature after the second wire drawing was changed at 500 ° C or less to investigate the influence on the average crystal grain size in the cross-sectional direction, austenite phase ratio, tensile strength, fatigue resistance, and corrosion resistance. However, the effect of the present invention was confirmed. Invention Example No. 50,51,5
2, the effect of the present invention is remarkable and the tensile strength is 1700.
It exceeds N / mm ² and exhibits strength and fatigue resistance comparable to high carbon steel. Invention Example No. In No. 49, the aging temperature is too low, and therefore improvement in strength and fatigue resistance cannot be expected. Invention Example No. In No. 53, the aging temperature is too high, and therefore improvement in fatigue resistance cannot be expected. As can be seen from the above examples, the superiority of the present invention example is clear.

【００４５】[0045]

【表１】 [Table 1]

【００４６】[0046]

【表２】 [Table 2]

【００４７】[0047]

【表３】 [Table 3]

【００４８】[0048]

【表４】 [Table 4]

【００４９】[0049]

【表５】 [Table 5]

【００５０】[0050]

【表６】 [Table 6]

【００５１】[0051]

【発明の効果】本発明により耐疲労・耐食性に優れた高
強度ステンレスワイヤロープ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。According to the present invention, it is possible to provide a high strength stainless wire rope having excellent fatigue resistance and corrosion resistance.
Industrially effective effects are brought about.

【図面の簡単な説明】[Brief description of drawings]

【図１】ワイヤロープの横断面方向の平均結晶粒径と耐
疲労性の関係を示す図である。FIG. 1 is a diagram showing a relationship between an average crystal grain size in a cross-sectional direction of a wire rope and fatigue resistance.

【図２】伸線加工の減面率とワイヤロープの強度の関係
を示す図である。FIG. 2 is a diagram showing a relationship between a reduction rate of wire drawing and strength of a wire rope.

【図３】伸線加工の減面率と鋼線の引張破断絞りの関係
を示す図である。FIG. 3 is a diagram showing the relationship between the area reduction rate of wire drawing and the tensile fracture drawing of steel wire.

【図４】伸線加工の減面率とワイヤロープの耐疲労性の
関係を示す図である。FIG. 4 is a diagram showing the relationship between the area reduction rate of wire drawing and the fatigue resistance of the wire rope.

【図５】ワイヤロープのオーステナイト相の量とＧ１，
Ｇ２の関係を示す図である。FIG. 5: Amount of austenite phase of wire rope and G1,
It is a figure which shows the relationship of G2.

【図６】Ｇ１，Ｇ２とワイヤロープの引張強さの関係を
示す図である。FIG. 6 is a diagram showing the relationship between G1 and G2 and the tensile strength of the wire rope.

───────────────────────────────────────────────────── フロントページの続き (72)発明者 村田 亘 山口県光市大字島田3434番地 新日本製鐵 株式会社光製鐵所内 (72)発明者 神田 康治 茨城県新治郡出島村大字宍倉5707 東京製 綱株式会社研究所内 (72)発明者 村上 卓也 東京都中央区日本橋室町２丁目３番14号 東京製綱株式会社内 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Wataru Murata 3434 Shimada, Hikari City, Yamaguchi Prefecture Inside the Nippon Steel Corporation Hikari Steel Works (72) Inventor Koji Kanda Dejima Village, Shinji-gun, Ibaraki Prefecture 5707 Shishikura Tokyo Tsuna Co., Ltd. Research Institute (72) Inventor Takuya Murakami 2-3-14 Nihonbashi Muromachi, Chuo-ku, Tokyo Tokyo Tsuna Tsuna Co., Ltd.

Claims (6)

【特許請求の範囲】[Claims] 【請求項１】 重量％で、 Ｃ ：０．１２％以下、 Ｓｉ：０．１％〜１．５％、 Ｍｎ：１．５％超〜８．０％、 Ｐ ：０．０３％以下、 Ｓ ：０．０１％以下、 Ｎｉ：３．５％〜７．５％、 Ｃｒ：２０．０％〜２８．０％、 Ｍｏ：０．１％〜３．０％以下 を含有し、下記式（１）で表されるＧ１の値が−１〜２
（％）で残部が実質的にＦｅおよび不可避的不純物から
なる合金組成で、横断面方向の平均結晶粒径が５μｍ以
下であり、引張強さが１５００Ｎ／mm² 以上であること
を特徴とする耐疲労・耐食性に優れた高強度ステンレス
ワイヤロープ。 Ｇ１＝０．６７Ｎｉ＋２０Ｃ＋０．３４Ｍｎ−０．４Ｃｒ−０．４Ｍｏ −０．６Ｓｉ＋３・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・・（１）1. By weight%, C: 0.12% or less, Si: 0.1% to 1.5%, Mn: more than 1.5% to 8.0%, P: 0.03% or less, S: 0.01% or less, Ni: 3.5% to 7.5%, Cr: 20.0% to 28.0%, Mo: 0.1% to 3.0% or less. The value of G1 represented by (1) is −1 to 2
(%) Is an alloy composition in which the balance substantially consists of Fe and unavoidable impurities, the average crystal grain size in the transverse direction is 5 μm or less, and the tensile strength is 1500 N / mm ² or more. A high-strength stainless wire rope with excellent fatigue and corrosion resistance. G1 = 0.67Ni + 20C + 0.34Mn-0.4Cr-0.4Mo-0.6Si + 3 ...・ ・ ・ ・ ・ ・ ・ (1) 【請求項２】 請求項１記載の成分にさらに重量％で、 Ｎ ：０．１％〜０．３％ を含有し、下記式（２）で表されるＧ２の値が−１〜２
（％）であることを特徴とする請求項１記載の耐疲労・
耐食性に優れた高強度ステンレスワイヤロープ。 Ｇ２＝０．６７Ｎｉ＋２０Ｃ＋２０Ｎ＋０．３４Ｍｎ−０．４Ｃｒ −０．４Ｍｏ−０．６Ｓｉ＋３・・・・・・・・・・・・・・・・・・・・・・・・・・・・（２）2. The component according to claim 1, further containing N: 0.1% to 0.3% by weight, and the value of G2 represented by the following formula (2) is -1 to 2.
(%) Is the fatigue resistance according to claim 1,
High-strength stainless wire rope with excellent corrosion resistance. G2 = 0.67Ni + 20C + 20N + 0.34Mn-0.4Cr-0.4Mo-0.6Si + 3 ... (2) 【請求項３】 請求項１或いは２記載の成分にさらに重
量％で、 Ｎｂ：０．０５％〜０．５０％、 Ｔｉ：０．０５％〜０．５０％ のうち１種または２種を含有し、下記式（３）で表され
るＧ３の値が−１〜２（％）で、鋼線の横断面方向の平
均結晶粒径が３μｍ未満であることを特徴とする請求項
１或いは２記載の耐疲労・耐食性に優れた高強度ステン
レスワイヤロープ。 Ｇ３＝０．６７Ｎｉ＋２０Ｃ＋２０Ｎ＋０．３４Ｍｎ−０．４Ｃｒ −０．４Ｍｏ−０．６Ｓｉ−０．９Ｔｉ−０．１Ｎｂ＋３・・・・（３）3. The component according to claim 1 or 2, further comprising 1% or 2% of Nb: 0.05% to 0.50% and Ti: 0.05% to 0.50% by weight. The value of G3 represented by the following formula (3) is -1 to 2 (%), and the average crystal grain size in the transverse direction of the steel wire is less than 3 µm. High-strength stainless wire rope with excellent fatigue and corrosion resistance as described in 2. G3 = 0.67Ni + 20C + 20N + 0.34Mn-0.4Cr-0.4Mo-0.6Si-0.9Ti-0.1Nb + 3 ... (3) 【請求項４】 請求項１，２または３の何れかに記載の
成分にさらに重量％で、 Ａｌ：０．０１％以下、 Ｃａ：０．００１％〜０．００４％ を含有し、鋼線の横断面方向の介在物の大きさが２０μ
ｍ以下であることを特徴とする請求項１，２または３の
何れかに記載の耐疲労性・耐食性に優れた高強度ステン
レスワイヤロープ。4. A steel wire containing the component according to claim 1, 2 or 3 in an amount of, by weight%, Al: 0.01% or less and Ca: 0.001% to 0.004%. The size of inclusions in the cross-sectional direction of
The high-strength stainless steel wire rope excellent in fatigue resistance and corrosion resistance according to claim 1, characterized in that it is m or less. 【請求項５】 請求項１，２，３または４の何れかに記
載の成分を有する熱間圧延のまま或いは熱処理後の線材
を、トータル減面率で５０％以上の伸線加工を施し、そ
の後、１０００℃〜１１５０℃の温度で熱処理後、引き
続き、減面率で８０％〜９５％の伸線加工を施し、その
後ワイヤロープにストランディングおよびクロージング
の撚り線加工を施すことを特徴とする耐疲労性・耐食性
に優れた高強度ステンレスワイヤロープの製造方法。5. A wire rod, which has been hot-rolled or has been heat-treated, having the component according to any one of claims 1, 2, 3 or 4 is subjected to wire drawing at a total area reduction of 50% or more, After that, after heat treatment at a temperature of 1000 ° C. to 1150 ° C., subsequently, a wire drawing process of 80% to 95% in area reduction is performed, and then a stranding process of stranding and closing is performed on the wire rope. A method for manufacturing high-strength stainless wire rope with excellent fatigue resistance and corrosion resistance. 【請求項６】 請求項５記載のワイヤロープに、さらに
２００〜４００℃の時効処理を施すことを特徴とする耐
疲労性・耐食性に優れた高強度ステンレスワイヤロープ
の製造方法。6. A method for producing a high-strength stainless wire rope having excellent fatigue resistance and corrosion resistance, which comprises subjecting the wire rope according to claim 5 to aging treatment at 200 to 400 ° C.