JP2618151B2 - High strength non-magnetic stainless steel wire rod - Google Patents
High strength non-magnetic stainless steel wire rodInfo
- Publication number
- JP2618151B2 JP2618151B2 JP4096664A JP9666492A JP2618151B2 JP 2618151 B2 JP2618151 B2 JP 2618151B2 JP 4096664 A JP4096664 A JP 4096664A JP 9666492 A JP9666492 A JP 9666492A JP 2618151 B2 JP2618151 B2 JP 2618151B2
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- cold
- strength
- workability
- ductility
- Prior art date
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Description
【０００１】[0001]
【産業上の利用分野】この発明は、高強度・非磁性でか
つ耐銹性と冷間加工性を必要とする用途に利用される高
Ｍｎステンレス鋼線材に関するもので、電子機器用シャ
フト材、自転車スポーク用線材、建築・建材用釘等に利
用される。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high Mn stainless steel wire used for applications requiring high strength, non-magnetic, rust resistance and cold workability, and a shaft material for electronic equipment, Used for bicycle spokes, nails for construction and building materials.
【０００２】[0002]
【従来の技術】電子機器用シャフト材は表面疵及び磁性
を嫌うことから高強度・非磁性及び耐銹性に優れている
ことが要求される。自転車スポーク材は軽量化、腐食防
止、塵付着の低減化、頭部加工の観点から高強度・非磁
性で、かつ、耐銹性及び冷間加工性に優れていることが
要求される。また、建築・建材用釘材は美観、耐銹性の
観点から鉄釘からステンレス釘へ転換されつつあり、Ｓ
ＵＳ３０４相当の耐銹性を持つ高強度材が要求されてい
る。これ等のために、ＳＵＳ３０４，ＳＵＳ３０５，Ｓ
ＵＳＸＭ７、高Ｎ含有の１８Ｃｒ−８Ｎｉ系や１８Ｃｒ
−１０Ｍｎ−５Ｎｉ系のステンレス鋼等が冷間加工によ
り加工強化され一部に供用されている。2. Description of the Related Art Shaft materials for electronic devices are required to have high strength, non-magnetism and excellent rust resistance because they dislike surface flaws and magnetism. Bicycle spoke materials are required to be high-strength, non-magnetic, and excellent in rust resistance and cold workability from the viewpoint of weight reduction, corrosion prevention, reduction of dust adhesion, and head processing. In addition, nails for construction and building materials are being changed from iron nails to stainless steel nails from the viewpoint of aesthetics and rust resistance.
There is a demand for a high-strength material having rust resistance equivalent to US304. For these reasons, SUS304, SUS305, S
USXM7, 18Cr-8Ni or 18Cr with high N content
-10Mn-5Ni-based stainless steel or the like is strengthened by cold working and is partially used.
【０００３】しかし、必ずしも満足できる状況にはな
く、さらに線材製造性のための熱間加工性や冷間加工性
に優れた安価な高強度・非磁性ステンレス鋼線材の供給
が要求されている現状にある。However, the situation is not always satisfactory, and there is a demand for the supply of inexpensive, high-strength, non-magnetic stainless steel wires excellent in hot workability and cold workability for wire manufacturability. It is in.
【０００４】冷間加工後高強度を有するためには高Ｃ化
及び高Ｎ化が有効であることが知られている。しかし、
Ｃの増加は炭化物を析出させ易く、炭化物起因による冷
間加工性劣化の課題がある。また、ＮについてはＣｒや
Ｍｎの増加により固溶量を増加させることにより、Ｎの
添加量の増加が図られる現状にあるが、ＣｒやＭｎの増
加は熱間加工性を害すると同時に強度の冷間加工後の延
性を低下させる課題がある。It is known that high C and high N are effective to have high strength after cold working. But,
An increase in C tends to cause carbide to precipitate, and there is a problem of deterioration of cold workability due to carbide. Further, as for N, the amount of N added can be increased by increasing the amount of solid solution by increasing Cr or Mn, but the increase of Cr or Mn impairs hot workability and at the same time increases strength. There is a problem of reducing ductility after cold working.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、熱間と冷間
における加工性課題と冷間加工後の強度及び延性課題を
解決し、高強度・非磁性ステンレス鋼線材を安価に供給
できる技術を提供するものである。SUMMARY OF THE INVENTION The present invention solves the problems of workability between hot and cold, and the strength and ductility after cold working, and provides a low-cost supply of high-strength, non-magnetic stainless steel wires. Is provided.
【０００６】[0006]
【課題を解決するための手段】本発明は熱間加工性と冷
間加工性及び冷間加工後の強度と延性に及ぼす材料構成
成分の影響を綿密に調査し、熱間加工性と冷間加工性が
良く冷間加工後も高強度、高延性をもつ材料を知見した
ことによる。特に、Ｎｂを添加することにより加工性を
害するＣｒ及びＭｎを増加することなく、鋳造時の気泡
発生を伴わずに鋼中に多量のＮを添加できることを知見
したことによる。DISCLOSURE OF THE INVENTION The present invention examines the effects of material components on hot workability and cold workability, and strength and ductility after cold work, and examines hot workability and cold workability. It is based on the finding that the material has good workability and high strength and high ductility even after cold working. In particular, it has been found that a large amount of N can be added to steel without increasing bubbles of Cr and Mn that impair workability by adding Nb and without generating bubbles during casting.
【０００７】すなわち、本発明は重量％で、Ｃ：０．０
７〜０．１２％、Ｓｉ：０．０５〜１．０％、Ｍｎ：
４．５〜１２．０％、Ｎｉ：２．５〜６．０％、Ｃｒ：
１６．０〜１９．５％、Ｃｕ：＜３．０％、Ｎｂ：０．
０５〜０．１５％、Ｎ：０．２０〜０．４０％、Ａｌ：
＜０．１％、残部Ｆｅ及び不可避的不純物からなり、か
つ、下記１式で規定されるαの値が０％以下を満足す
る、熱間加工性と冷間加工性及び強加工度の冷間加工後
にも高延性を有する高強度・非磁性ステンレス鋼線材で
ある。 α＝ 1.6Ｃｒ＋0.77Ｓｉ＋0.0128×〔Ｍｎ〕2 −0.11Ｍｎ−Ｎｉ−24.5Ｃ−18.4Ｎ−20.6 ……………１式That is, in the present invention, C: 0.0% by weight.
7 to 0.12%, Si: 0.05 to 1.0%, Mn:
4.5 to 12.0%, Ni: 2.5 to 6.0%, Cr:
16.0 to 19.5%, Cu: <3.0%, Nb: 0.
05 to 0.15%, N: 0.20 to 0.40%, Al:
<0.1%, and the balance Fe and unavoidable impurities, and the value of α defined by the equation (1) below satisfies 0% or less, hot workability and cold workability and strong working of the cold It is a high-strength non-magnetic stainless steel wire that has high ductility even after hot working. α = 1.6Cr + 0.77Si + 0.0128 × [Mn] 2 -0.11Mn-Ni-24.5C-18.4N-20.6
【０００８】以下に本発明の範囲を上記に限定した理由
を述べる。Ｃは伸線加工後の強度を確保するために、
０．０７％以上添加する。過剰の添加は固溶化処理後の
冷却過程において炭化物を析出し、６０％を超える冷間
加工後の延性を著しく低下させる。このため、上限を
０．１２％に限定した。The reason for limiting the scope of the present invention to the above will be described below. C is to secure the strength after wire drawing.
Add 0.07% or more. Excessive addition precipitates carbides during the cooling process after the solution treatment, and significantly reduces ductility after cold working exceeding 60%. For this reason, the upper limit was limited to 0.12%.
【０００９】Ｓｉは脱酸のために添加する。０．０５％
未満ではその効果がないため、下限を０．０５％にし
た。また、過剰の添加は熱間加工性を劣化させるため、
上限を１．０％に限定した。[0009] Si is added for deoxidation. 0.05%
If it is less than 10%, the lower limit is set to 0.05%. In addition, since excessive addition deteriorates hot workability,
The upper limit was limited to 1.0%.
【００１０】Ｍｎは冷間加工後の非磁性及び高強度を確
保するために４．５％以上添加する。過剰の添加は通常
の常識に反しフェライトを生成し易くなることと、熱間
加工性、耐銹性及び６０％以上の冷間加工後の延性を劣
化させるため、上限を１２．０％に限定した。Mn is added in an amount of 4.5% or more in order to secure non-magnetic properties and high strength after cold working. Excessive addition, contrary to common sense, tends to form ferrite and degrades hot workability, rust resistance and ductility after cold working of 60% or more, so the upper limit is limited to 12.0%. did.
【００１１】Ｎｉは冷間加工後の非磁性及び延性を確保
するために２．５％以上添加する。過剰の添加は冷間加
工後の強度を低くするため、上限を６．０％に限定し
た。Ni is added in an amount of 2.5% or more in order to ensure non-magnetism and ductility after cold working. Excessive addition lowers the strength after cold working, so the upper limit is limited to 6.0%.
【００１２】Ｃｒは耐銹性のために１６．０％以上添加
する。過剰の添加は熱間加工性を劣化させると同時に固
溶化処理後の冷却過程において炭化物を析出させて６０
％以上の冷間加工後の延性を劣化させるため、上限を１
９．５％以下に限定した。[0012] Cr is added at 16.0% or more for rust resistance. Excessive addition deteriorates the hot workability and at the same time precipitates carbides in the cooling process after the solution treatment, causing
% In order to degrade ductility after cold working of at least 1%.
Limited to 9.5% or less.
【００１３】本発明に対するＣｕの効果は少ないため添
加しても構わないが、過剰の添加は熱間加工性を低下さ
せると同時に冷間加工後の強度を低くするため上限を
３．０％に限定した。Although the effect of Cu on the present invention is small, it may be added. However, an excessive addition lowers the hot workability and at the same time lowers the strength after cold working, so that the upper limit is set to 3.0%. Limited.
【００１４】Ｎｂは図１に示すように多量のＮを含有す
る鋼において鋳造時のＮ起因の気泡発生を抑制する。図
中のＡ−Ｂ線の上部領域では気泡が発生し、下部領域で
は気泡の発生は無い。このため、本発明では気泡発生抑
制のためにＮｂは０．０５％以上添加する。過剰の添加
はＮｂ系の炭窒化物を析出するようになり、熱間加工性
を劣化させるため、上限を０．１５％に限定した。Nb suppresses the generation of bubbles due to N during casting in steel containing a large amount of N as shown in FIG. Air bubbles are generated in the upper region of the line AB in the drawing, and no air bubbles are generated in the lower region. Therefore, in the present invention, Nb is added in an amount of 0.05% or more to suppress the generation of bubbles. Excessive addition causes Nb-based carbonitrides to precipitate, deteriorating hot workability, so the upper limit was limited to 0.15%.
【００１５】Ｎは冷間加工後の非磁性と高強度を得るた
めに０．２０％以上添加する。過剰の添加は熱間加工性
と６０％以上の冷間加工後の延性を劣化させるため、上
限を０．４０％に限定した。N is added in an amount of 0.20% or more in order to obtain non-magnetic properties and high strength after cold working. Excessive addition deteriorates hot workability and ductility after cold working of 60% or more, so the upper limit was limited to 0.40%.
【００１６】Ａｌは脱酸のために添加するが、過剰の添
加は介在物の増加と熱間加工性を劣化させるため、上限
を０．１％以下に限定した。Al is added for the purpose of deoxidation. However, since excessive addition increases inclusions and deteriorates hot workability, the upper limit is limited to 0.1% or less.
【００１７】αの値は冷間加工後の磁性と構成成分の関
係を調査し得た関係式で、特にＭｎの効果に特徴があ
る。すなわち、Ｍｎは８．６％で最もオーステナイトを
安定にするがその上下の量ではむしろオーステナイトを
不安定にする。αの値が０％以上では６０％以上の冷間
加工を施すと磁性が認められるようになる。このため上
限値を０％以下に限定した。The value of α is a relational expression obtained by investigating the relationship between the magnetism after cold working and the constituent components, and is particularly characterized by the effect of Mn. That is, Mn stabilizes most austenite at 8.6%, but the amount above and below Mn makes austenite unstable. When the value of α is 0% or more, magnetism is recognized when cold working of 60% or more is performed. Therefore, the upper limit is limited to 0% or less.
【００１８】[0018]
【実施例】表１に本発明例と比較例の化学成分を、表２
に本発明例と比較例の熱間加工性、冷間加工性、伸線加
工後の強度及び延性、耐銹性及び磁性を示す。EXAMPLES Table 1 shows the chemical components of the present invention and comparative examples, and Table 2
The hot workability, cold workability, strength and ductility after wire drawing, rust resistance and magnetism of the inventive examples and comparative examples are shown in FIG.
【００１９】[0019]
【表１】 [Table 1]
【００２０】[0020]
【表２】 [Table 2]
【００２１】[0021]
【表３】 [Table 3]
【００２２】[0022]
【表４】 [Table 4]
【００２３】いずれの供試材もステンレス鋼の通常の精
錬工程（電気炉または転炉溶解後真空或いはアルゴン／
酸素脱酸処理による精錬）で溶解・精錬後連続鋳造によ
り製造したビレットを分塊工程を経ずに、均熱処理後ま
たはそのまま線材圧延した。また、各特性の評価は下記
の方法で行った。All of the test materials were prepared by the ordinary refining process of stainless steel (after melting in an electric furnace or a converter, vacuum or argon /
The billet produced by continuous casting after melting and refining by oxygen deoxidation treatment) was subjected to soaking or rolled as it was, without going through a lumping step. The evaluation of each characteristic was performed by the following method.
【００２４】（１）熱間加工性 １２５０℃の加熱後冷却過程において高速引張試験を実
施した。熱間加工性の評価は冷却過程の１０００℃にお
ける引張破断部の絞り値（％）で評価した。絞り値は高
い値ほど熱間加工性が良好で６０％以上であれば割れ等
の欠陥を発生することなく線材圧延が可能で本発明は６
０％以上を目標とした。 （２）気泡 鋳片の横断面観察により気泡の発生有無を評価した。本
発明は鋳片中に気泡発生がないことを目標とした。 （３）冷間加工性 ５．５mm線径の線材を２mm線径まで伸線加工（８６．８
％の冷間加工）し、伸線破断の有無により冷間加工性を
評価した。本発明は破断なく伸線可能であることを目標
とした。(1) Hot workability A high-speed tensile test was performed in the cooling process after heating at 1250 ° C. The evaluation of the hot workability was evaluated by the drawing value (%) of the tensile fracture portion at 1000 ° C. in the cooling process. The higher the drawing value, the better the hot workability, and if it is 60% or more, the wire rod can be rolled without generating defects such as cracks.
The target was 0% or more. (2) Bubbles The presence or absence of bubbles was evaluated by observing the cross section of the cast slab. The present invention aimed at the absence of air bubbles in the slab. (3) Cold workability Wire drawing of 5.5 mm wire diameter to 2 mm wire diameter (86.8)
% Cold work), and the cold workability was evaluated based on the presence or absence of wire breakage. An object of the present invention is to be able to draw without breaking.
【００２５】（４）伸線加工後の強度及び延性 ５．５mm線径の線材を３mm線径まで伸線加工（７０．２
％冷間加工）後引張試験片を採取し、引張破断させた。
その時の引張強度と破断絞り値で評価した。本発明は強
度１７００Ｎ／mm2 以上で、かつ、絞り値５０％以上を
目標とした。 （５）磁性 ５．５mm線径の線材を３mm線径まで伸線加工（７０．２
％冷間加工）後透磁率を測定し評価した。本発明は透磁
率１．０５％以下を目標とした。(4) Strength and ductility after wire drawing A wire having a diameter of 5.5 mm is drawn to a wire diameter of 3 mm (70.2).
% Cold work), and a tensile test piece was collected and subjected to tensile breaking.
The evaluation was made based on the tensile strength at that time and the squeeze value at break. The present invention aims at a strength of 1700 N / mm 2 or more and an aperture value of 50% or more. (5) Magnetic wire drawing of 5.5 mm wire diameter to 3 mm wire diameter (70.2
% Cold working), and the magnetic permeability was measured and evaluated. The present invention aims at a magnetic permeability of 1.05% or less.
【００２６】本発明例No．１，２と比較例No．１８，１
９はＣの影響を調査したものである。Ｃが本発明範囲未
満のNo．１８は冷間加工後の強度、延性が本発明に比較
し劣っている。また、Ｃが本発明例の範囲を超えるNo．
１９は冷間加工性が悪く７０．２％の伸線加工ができ
ず、伸線加工時に破断した。上記から本発明の優位性が
明らかである。Inventive Example No. 1, 2 and Comparative Example No. 18,1
9 investigates the effect of C. C is less than the range of the present invention. No. 18 is inferior in strength and ductility after cold working as compared with the present invention. In addition, C. is out of the range of the present invention example.
In No. 19, the cold workability was poor and wire drawing of 70.2% could not be performed, and the wire was broken during wire drawing. The advantages of the present invention are apparent from the above.
【００２７】本発明例No．３，４と比較例No．２０，２
１はＳｉの影響を調査したものである。Ｓｉが本発明範
囲未満のNo．２０は冷間加工後の延性が本発明に比較し
劣っている。また、Ｓｉが本発明の範囲を超えるNo．２
１は冷間加工性が悪く７０．２％の伸線加工ができず、
伸線加工時に破断した。また、熱間加工性も劣っており
本発明の優位性が明らかである。Inventive Example No. Nos. 3 and 4 and Comparative Example Nos. 20,2
1 is a result of investigating the influence of Si. No. of Si less than the range of the present invention. No. 20 is inferior to the present invention in ductility after cold working. In addition, when Si exceeds No. 2
No. 1 has poor cold workability and cannot draw 70.2% wire.
It broke during wire drawing. Further, the hot workability is inferior, and the superiority of the present invention is apparent.
【００２８】本発明例No．５，６と比較例No．２２，２
３はＭｎの影響を調査したものである。Ｍｎが本発明範
囲未満のNo．２２は冷間加工後の強度が本発明に比較し
劣っている。また、Ｍｎが本発明の範囲を超えるNo．２
３は熱間加工性、冷間加工後の延性及び伸線性に劣って
おり本発明の優位性が明らかである。Inventive Example No. Nos. 5 and 6 and Comparative Example Nos. 22,2
No. 3 investigates the effect of Mn. No. with Mn less than the range of the present invention. No. 22 is inferior in strength after cold working as compared with the present invention. In addition, the Mn having a Mn exceeding the range of the present invention. 2
No. 3 is inferior in hot workability, ductility after cold working and wire drawability, and the superiority of the present invention is apparent.
【００２９】本発明例No．７，８と比較例No．２４，２
５はＮｉの影響を調査したものである。Ｎｉが本発明範
囲未満のNo．２４は熱間加工性、冷間加工後の延性、伸
線加工性及び透磁率が本発明に比較し劣っている。ま
た、Ｎｉが本発明の範囲を超えるNo．２５は冷間加工後
の強度及び延性が劣っており本発明の優位性が明らかで
ある。Inventive Example No. 7 and 8 and Comparative Example Nos. 24,2
5 is the result of investigating the influence of Ni. No. of Ni less than the range of the present invention. No. 24 is inferior to the present invention in hot workability, ductility after cold working, wire drawing workability, and magnetic permeability. Further, when the Ni content exceeds the range of the present invention, the Ni. No. 25 is inferior in strength and ductility after cold working, and the superiority of the present invention is apparent.
【００３０】本発明例No．９，１０と比較例No．２６，
２７はＣｒの影響を調査したものである。Ｃｒが本発明
範囲未満のNo．２６は冷間加工後の強度及び延性が本発
明に比較し劣っている。また、Ｃｒが本発明の範囲を超
えるNo．２７は熱間加工性と冷間加工後の延性が劣って
おり本発明の優位性が明らかである。Inventive Example No. 9 and 10 and Comparative Example Nos. 26,
Reference numeral 27 indicates the effect of Cr. No. Cr whose Cr content is less than the range of the present invention. No. 26 is inferior in strength and ductility after cold working as compared with the present invention. In addition, when the Cr content exceeds the range of the present invention, No. 27 is inferior in hot workability and ductility after cold work, and the superiority of the present invention is apparent.
【００３１】本発明例No．１１と比較例No．２８はＣｕ
の影響を調査したものである。Ｃｕが本発明の範囲を超
えるNo．２８は熱間加工性、冷間加工後の強度及び冷間
加工性が劣っている。また、No．２８はα値が０％以上
であり透磁率も劣っており本発明の優位性が明らかであ
る。Inventive Example No. 11 and Comparative Example No. 28 is Cu
The effect of this was investigated. No. Cu exceeding the range of the present invention. No. 28 is inferior in hot workability, strength after cold work, and cold workability. No. In No. 28, the α value is 0% or more and the magnetic permeability is inferior, and the superiority of the present invention is apparent.
【００３２】本発明例No．１２，１３と比較例No．２
９，３０，３１はＮｂの影響を調査したものである。Ｎ
ｂが本発明範囲未満のNo．２９，３０は鋳片中に気泡が
発生し、加えて熱間加工性、冷間加工後の延性及び冷間
加工性が本発明に比較し劣っている。また、α値が０以
上であり透磁率も本発明に劣っている。Ｎｂが本発明の
範囲を超えるNo．３１は熱間加工性と冷間加工後の延性
が劣っており本発明の優位性が明らかである。Inventive Example No. Nos. 12 and 13 and Comparative Example Nos. 2
9, 30, and 31 investigate the effect of Nb. N
b is less than the range of the present invention. In Nos. 29 and 30, bubbles are generated in the slab, and in addition, hot workability, ductility after cold working and cold workability are inferior to those of the present invention. The α value is 0 or more, and the magnetic permeability is inferior to that of the present invention. No. Nb exceeding the range of the present invention. No. 31 is inferior in hot workability and ductility after cold work, and the superiority of the present invention is apparent.
【００３３】本発明例No．１４，１５と比較例No．３
２，３３はＮの影響を調査したものである。Ｎが本発明
範囲未満のNo．３２は冷間加工後の強度が本発明に比較
し劣っている。また、Ｎが本発明の範囲を超えるNo．３
３は熱間加工性と冷間加工後の延性が劣っており本発明
の優位性が明らかである。Inventive Example No. Nos. 14 and 15 and Comparative Example Nos. 3
Nos. 2 and 33 investigate the effects of N. N is less than the range of the present invention. No. 32 is inferior in strength after cold working as compared with the present invention. Further, when N exceeds the range of the present invention, 3
No. 3 is inferior in hot workability and ductility after cold work, and the superiority of the present invention is apparent.
【００３４】本発明例No．１６，１７と比較例No．３
４，３５は本発明全元素の下限及び上限の影響を調査し
たものである。全ての元素が本発明の下限未満のNo．３
４は伸線後の強度が本発明に比較し劣っている。全ての
元素が本発明の上限を超えるNo．３５は熱間加工性、伸
線性が劣っている。また、７０．２％の伸線加工ができ
ず破断しており本発明の優位性が明らかである。Inventive Example No. Nos. 16, 17 and Comparative Example No. 3
Nos. 4 and 35 investigate the influence of the lower and upper limits of all the elements of the present invention. All elements are No. less than the lower limit of the present invention. 3
No. 4 is inferior in strength after wire drawing to the present invention. All elements exceed the upper limit of the present invention. No. 35 has poor hot workability and drawability. In addition, the wire could not be drawn by 70.2%, and the wire was broken. This clearly shows the superiority of the present invention.
【００３５】比較例No．３６はα値のみが本発明の上限
を超えるもので、熱間加工性、冷間加工後の延性及び冷
間加工性が劣っており本発明の優位性が明らかである。Comparative Example No. In the case of No. 36, only the α value exceeds the upper limit of the present invention, and the hot workability, ductility after cold working and cold workability are inferior, and the superiority of the present invention is apparent.
【００３６】[0036]
【発明の効果】本発明によれば、熱間加工性課題と冷間
加工性及び強度の冷間加工後の延性課題を解決し、高強
度・非磁性ステンレス鋼線材を安価に供給することが可
能で産業上有効な効果がもたらされる。According to the present invention, the problem of hot workability and the problem of ductility after cold working of cold workability and strength can be solved, and a high-strength non-magnetic stainless steel wire can be supplied at low cost. Possible and industrially effective effects are provided.
【図１】ＮｂとＮ関係より鋳造時に発生する気泡の発生
の有無を示した図表である。FIG. 1 is a table showing the presence or absence of bubbles generated during casting based on the relationship between Nb and N.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 河村 敏彦 光市大字島田3434番地 新日本製鐵株式 会社 光製鐵所内 (56)参考文献 特開 昭53−117617（ＪＰ，Ａ) ────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Toshihiko Kawamura 3434 Shimada, Hikari-shi Nippon Steel Corporation Hikari Works (56) References
Claims (1)
で規定されるαの値が０％以下を満足することを特徴と
する高強度・非磁性ステンレス鋼線材。 α＝ 1.6Ｃｒ＋0.77Ｓｉ＋0.0128×〔Ｍｎ〕2 −0.11Ｍｎ−Ｎｉ−24.5Ｃ−18.4Ｎ−20.6 ……………１式C: 0.07 to 0.12%, Si: 0.05 to 1.0%, Mn: 4.5 to 12.0%, Ni: 2.5 to 6. 0%, Cr: 16.0 to 19.5%, Cu: <3.0%, Nb: 0.05 to 0.15%, N: 0.20 to 0.40%, Al: <0.1 %, The balance being Fe and unavoidable impurities, and wherein the value of α defined by the following equation ( 1) satisfies 0% or less. α = 1.6Cr + 0.77Si + 0.0128 × [Mn] 2 -0.11Mn-Ni-24.5C-18.4N-20.6
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4096664A JP2618151B2 (en) | 1992-04-16 | 1992-04-16 | High strength non-magnetic stainless steel wire rod |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4096664A JP2618151B2 (en) | 1992-04-16 | 1992-04-16 | High strength non-magnetic stainless steel wire rod |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05295486A JPH05295486A (en) | 1993-11-09 |
| JP2618151B2 true JP2618151B2 (en) | 1997-06-11 |
Family
ID=14171088
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4096664A Expired - Fee Related JP2618151B2 (en) | 1992-04-16 | 1992-04-16 | High strength non-magnetic stainless steel wire rod |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2618151B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7604860B2 (en) | 2004-05-25 | 2009-10-20 | Korea Sangsa Co., Ltd. | High tensile nonmagnetic stainless steel wire for overhead electric conductor, low loss overhead electric conductor using the wire, and method of manufacturing the wire and overhead electric conductor |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999032682A1 (en) * | 1997-12-23 | 1999-07-01 | Allegheny Ludlum Corporation | Austenitic stainless steel including columbium |
| JP4212553B2 (en) * | 2002-05-08 | 2009-01-21 | 新日鐵住金ステンレス株式会社 | High-strength stainless steel wire with excellent twist value and rigidity and manufacturing method thereof |
| KR100507904B1 (en) * | 2003-01-10 | 2005-08-10 | 한국전기연구원 | Nonmagnetic stainless steel wire for overhead electric conductor, overhead electric conductor using the same, and manufacturing method of them respectively |
| MX365548B (en) | 2007-11-29 | 2019-06-07 | Ati Properties Llc | Lean austenitic stainless steel. |
| US8337749B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel |
| AU2008341063C1 (en) * | 2007-12-20 | 2014-05-22 | Ati Properties Llc | Austenitic stainless steel low in nickel containing stabilizing elements |
| US8877121B2 (en) | 2007-12-20 | 2014-11-04 | Ati Properties, Inc. | Corrosion resistant lean austenitic stainless steel |
| JP6560881B2 (en) * | 2015-03-26 | 2019-08-14 | 日鉄ステンレス株式会社 | Extremely low permeability stainless steel wire, as well as steel wire and deformed wire with excellent durability |
| KR101858851B1 (en) | 2016-12-16 | 2018-05-17 | 주식회사 포스코 | High strength wire rod having excellent ductility and method for manufacturing same |
| CN109112431B (en) * | 2018-10-10 | 2022-09-09 | 温州市安硕新材料有限公司 | A kind of non-magnetic stainless steel cold-rolled sheet for deep drawing and preparation method thereof |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6037182B2 (en) * | 1977-03-24 | 1985-08-24 | 日本冶金工業株式会社 | High strength austenitic stainless steel with excellent corrosion resistance |
| JPS59205451A (en) * | 1983-05-09 | 1984-11-21 | Nippon Yakin Kogyo Co Ltd | Manufacturing method of high-strength non-magnetic steel |
| JPS60221519A (en) * | 1984-04-10 | 1985-11-06 | Kobe Steel Ltd | Production of austenitic stainless steel having high corrosion resistance and high strength |
| JPH0653892B2 (en) * | 1986-06-12 | 1994-07-20 | 鈴木金属工業株式会社 | Method for producing high strength non-magnetic stainless steel |
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1992
- 1992-04-16 JP JP4096664A patent/JP2618151B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7604860B2 (en) | 2004-05-25 | 2009-10-20 | Korea Sangsa Co., Ltd. | High tensile nonmagnetic stainless steel wire for overhead electric conductor, low loss overhead electric conductor using the wire, and method of manufacturing the wire and overhead electric conductor |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH05295486A (en) | 1993-11-09 |
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