JPH06235049A - High strength nonmagnetic stainless steel and its production - Google Patents
High strength nonmagnetic stainless steel and its productionInfo
- Publication number
- JPH06235049A JPH06235049A JP2152993A JP2152993A JPH06235049A JP H06235049 A JPH06235049 A JP H06235049A JP 2152993 A JP2152993 A JP 2152993A JP 2152993 A JP2152993 A JP 2152993A JP H06235049 A JPH06235049 A JP H06235049A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- present
- cold working
- aging
- hardness
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、高強度非磁性と冷間加
工性を必要とする用途に利用される時効型の高Ｍｎステ
ンレス鋼線材及び板等に関するもので、電子機器用シャ
フト材、自転車スポーク用線、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 an aging type high Mn stainless steel wire rod and plate used for applications requiring high strength non-magnetism and cold workability, such as shaft material for electronic equipment, Used for bicycle spoke wire, nails for construction and building materials, etc.
【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鋼釘へ転換されつつあり、ＳＵ
Ｓ３０４相当の耐銹性を持つ高硬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
り加工硬化され、一部に供用されている。しかし、必ず
しも満足できる状況にはなく、さらに高強度の非磁性ス
テンレス鋼の供給が要求されている現状にある。通常、
高強度を出すために冷間加工後、時効処理が施される。
しかし、１８Ｃｒ−１０Ｍｎ−５Ｎｉ系や１８Ｃｒ−１
５Ｍｎ−１Ｎｉ系等の高Ｍｎステンレス鋼の時効硬化代
は冷間加工度にもよるが、ビッカース硬度にして、高々
５０程度にあり、さらに冷間加工後の硬度が高く、かつ
時効硬化量の大きい材料が望まれている。2. Description of the Related Art A shaft material for electronic equipment is required to have high strength non-magnetic property and excellent rust resistance because it does not like surface defects and magnetism. The bicycle spoke material is required to be high-strength non-magnetic, excellent in rust resistance and cold workability from the viewpoints of weight reduction, corrosion prevention, reduction of dust adhesion, and head processing. In addition, nail materials for construction and building materials are being converted from iron nails to stainless steel nails from the viewpoint of aesthetics and rust resistance.
A high hardness material having rust resistance equivalent to S304 is required. For these, SUS304, SUS305, S
USXM7, 18Cr-8Ni system and 18Cr containing high N
-10Mn-5Ni type stainless steel or the like is work-hardened by cold working and is partially used. However, the situation is not always satisfactory, and the supply of higher strength non-magnetic stainless steel is required. Normal,
Aging treatment is performed after cold working to obtain high strength.
However, 18Cr-10Mn-5Ni and 18Cr-1
Although the age hardening margin of high Mn stainless steel such as 5Mn-1Ni system depends on the cold working degree, it has a Vickers hardness of about 50 at most, and the hardness after cold working is high and the age hardening amount is high. Larger materials are desired.
【０００３】[0003]
【発明が解決しようとする課題】本発明は冷間加工後高
強度を有すると同時に時効処理を施した場合に時効硬化
量の高い高強度非磁性ステンレス鋼線材及び板及びその
製造方法を提供することを目的とするものである。The present invention provides a high-strength non-magnetic stainless steel wire rod and plate having high strength after cold working and high aging hardening amount when subjected to aging treatment, and a manufacturing method thereof. That is the purpose.
【０００４】[0004]
【課題を解決するための手段、作用】本発明は上記課題
の解決に当たり、冷間加工度と強度及び冷間加工後の時
効硬化量におよぼす材料構成成分の影響を綿密に調査
し、高Ｍｎ、高Ｎのステンレス鋼線材において、Ｍｏ及
びＰ添加が非常に有効であることを知見したことによ
る。Means for Solving the Problems In solving the above problems, the present invention scrutinizes the effects of the material constituents on the cold workability and strength and the age-hardening amount after cold working to obtain a high Mn content. , It was found that addition of Mo and P is very effective in high N stainless steel wire.
【０００５】すなわち、本発明の要旨とするところは下
記のとおりである。 （１） 重量％で、 Ｃ：０．０３〜０．１２％ Ｓｉ：０．０５〜１．０％ Ｍｎ：１０．０〜１７．０％ Ｐ：０．０４〜０．１０％ Ｎｉ：０．５〜６．０％ Ｃｒ：１６．０〜１９．５％ Ｍｏ：０．５〜２．５％ Ｎ：０．２５〜０．３４％ Ａｌ：０．００１〜０．１％ を含有し、さらに必要に応じて２．０％以下のＣｕを含
有し、かつ１式で規定されるαの値が０以下である高強
度非磁性ステンレス鋼。That is, the gist of the present invention is as follows. (1) By weight%, C: 0.03 to 0.12% Si: 0.05 to 1.0% Mn: 10.0 to 17.0% P: 0.04 to 0.10% Ni: 0 0.5 to 6.0% Cr: 16.0 to 19.5% Mo: 0.5 to 2.5% N: 0.25 to 0.34% Al: 0.001 to 0.1% A high-strength non-magnetic stainless steel containing 2.0% or less of Cu if necessary and having an α value of 0 or less defined by the formula 1.
【０００６】α＝１．６×Ｃｒ＋０．７７×Ｓｉ＋１．
９４×Ｍｏ＋０．０１２８×〔Ｍｎ〕2−０．１１×Ｍ
ｎ−Ｎｉ−２４．５×Ｃ−１８．４×Ｎ−２０．６…１
式 （２） さらに前記高硬度非磁性ステンレス鋼のビッカ
ース硬さが５５０以上、かつ透磁率が１．０５以下であ
る高強度非磁性ステンレス鋼。 （３） 前記（１）または（２）記載の高硬度非磁性ス
テンレス鋼を２０％以上９０％以下の冷間加工（伸線加
工）し、続いて時効処理温度〔Ｔ〕（℃）と時効時間
〔Ｈ〕（ｍｉｎ）の関係において、 ５００−８５×ｌｏｇＨ ≦Ｔ≦６００−２５×ｌｏｇ
Ｈ １≦Ｈ≦１２０ の範囲の時効処理を施すことを特徴とする高強度非磁性
ステンレス鋼の製造方法。Α = 1.6 × Cr + 0.77 × Si + 1.
94 x Mo + 0.0128 x [Mn] 2 -0.11 x M
n-Ni-24.5 x C-18.4 x N-20.6 ... 1
Formula (2) A high-strength nonmagnetic stainless steel in which the high-hardness nonmagnetic stainless steel has a Vickers hardness of 550 or more and a magnetic permeability of 1.05 or less. (3) Cold working (wire drawing) of 20% or more and 90% or less of the high hardness non-magnetic stainless steel according to (1) or (2) above, followed by aging treatment temperature [T] (° C) and aging In the relation of time [H] (min), 500-85 × log H ≦ T ≦ 600-25 × log
A method for producing a high-strength non-magnetic stainless steel, which comprises subjecting an aging treatment within a range of H 1 ≦ H ≦ 120.
【０００７】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、
０．０３％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、冷間加工後の延性を著しく低下させるた
め、上限を０．１２％に限定した。The reason why the scope of the present invention is limited to the above is described below. C is to secure the strength after wire drawing,
Add 0.03% or more. Excessive addition deteriorates the hot workability and at the same time precipitates carbides in the cooling process after the solution treatment and significantly reduces the ductility after the cold working. Therefore, the upper limit was set to 0.12%.
【０００８】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及び冷間加工性を劣
化させるため、上限を１．０％に限定した。Ｍｎは冷間
加工後の非磁性及び強度を確保するために１０．０％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
を生成し易くすることと、熱間加工性及び冷間加工後の
延性を劣化させるため、上限を１７．０％に限定した。Si is added for deoxidation. 0.05%
If it is less than 0.1%, the effect is not obtained. Moreover, since an excessive addition deteriorates the hot workability and the cold workability, the upper limit was limited to 1.0%. Mn is added in an amount of 10.0% or more in order to ensure non-magnetic property and strength after cold working. Excessive addition makes it easy to form ferrite contrary to common sense and deteriorates hot workability and ductility after cold working, so the upper limit was set to 17.0%.
【０００９】Ｐは冷間加工後の時効硬化量を増加させる
ために０．０４％以上添加する。過剰の添加は製造性の
劣化と冷間加工後の延性を低下させるため、上限を０．
１０％に限定した。Ｎｉは冷間加工後の非磁性及び延性
を確保するために０．５％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。P is added in an amount of 0.04% or more in order to increase the amount of age hardening after cold working. Since excessive addition deteriorates manufacturability and reduces ductility after cold working, the upper limit is set to 0.
Limited to 10%. Ni is added in an amount of 0.5% or more in order to ensure non-magnetism and ductility after cold working. Since the excessive addition lowers the strength after cold working, the upper limit was limited to 6.0%.
【００１０】Ｃｒは冷間加工後の高耐銹性を得るために
１６．０％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させ、冷間加工後の延性
を劣化させるため、上限を１９．５％に限定した。Ｍｏ
は冷間加工後の硬度及び時効硬化量の増加と高耐銹性及
び応力腐食割れ防止のために０．５％以上添加する。過
剰の添加は冷間加工性を劣化させるため、上限を１．５
％に限定した。Cr is added in an amount of 16.0% or more in order to obtain high rust resistance after cold working. Excessive addition causes carbides to precipitate during the cooling process after the solution treatment and deteriorates the ductility after cold working, so the upper limit was limited to 19.5%. Mo
Is added in an amount of 0.5% or more in order to increase the hardness and the amount of age hardening after cold working, to have high rust resistance and to prevent stress corrosion cracking. Since excessive addition deteriorates the cold workability, the upper limit is 1.5.
Limited to%.
【００１１】本発明に対するＣｕの効果は少なく、添加
しても構わないが、過剰の添加は冷間加工後の硬度を低
くするため上限を２．０％に限定した。Ｎは冷間加工後
の非磁性と高硬度を得るために０．２５％以上添加す
る。過剰の添加は冷間加工後の延性を劣化させるため上
限を０．３４％に限定した。Ａｌは脱酸のために０．０
０１％以上添加するが、過剰の添加は介在物の増加によ
り冷間加工性を劣化させるため上限を０．１％に限定し
た。The effect of Cu on the present invention is small, and Cu may be added, but the upper limit is limited to 2.0% because excessive addition lowers the hardness after cold working. N is added in an amount of 0.25% or more in order to obtain non-magnetic property and high hardness after cold working. Excessive addition deteriorates the ductility after cold working, so the upper limit was limited to 0.34%. Al is 0.0 because of deoxidation.
Although it is added in an amount of 01% or more, an excessive addition deteriorates the cold workability due to an increase in inclusions, so the upper limit was limited to 0.1%.
【００１２】αは冷間加工後の磁性と構成成分の関係を
調査して得た関係式で、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
安定にする効果がある。αが０超では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α
の上限値を０に限定した。Α is a relational expression obtained by investigating the relationship between magnetism and constituent components after cold working, and is particularly characterized by the effect of Mn.
That is, Mn stabilizes the austenite most at 8.6%, but the amount above and below it has the effect of making the austenite unstable. When α is more than 0, magnetism comes to be recognized when cold working of 60% or more is performed. Therefore α
The upper limit of is limited to 0.
【００１３】冷間加工は時効後の高硬度を得るために２
０％以上行う。冷間加工度が大き過ぎると欠陥を生じ、
延性が劣化するため上限を９０％に限定した。時効処理
は、時効処理温度〔Ｔ〕（℃）と時間〔Ｈ〕（ｍｉｎ）
の関係において、 ５００−８５×ｌｏｇＨ≦Ｔ≦６００−２５×ｌｏｇＨ １≦Ｈ≦１２０ の範囲の下限値未満では時効による硬化代が小さく、ま
た上限を超える範囲ではかえって軟化するため、時効温
度及び時間を上記範囲に限定した。Cold working is performed in order to obtain high hardness after aging.
Perform 0% or more. If the cold working degree is too high, defects will occur,
Since the ductility deteriorates, the upper limit was limited to 90%. The aging treatment is the aging treatment temperature [T] (° C) and time [H] (min).
In the relationship of 500-85 × logH ≦ T ≦ 600-25 × logH 1 ≦ H ≦ 120, the hardening margin due to aging is small if it is less than the lower limit value, and if it exceeds the upper limit, it rather softens, so that the aging temperature and The time was limited to the above range.
【００１４】[0014]
【実施例】次に、本発明の優位性を実施例と比較例を用
いて具体的に説明する。表１、表２（表１のつづき）に
本発明例と比較例の化学成分を、表３、表４（表３のつ
づき）に冷間加工後の硬度及び時効処理後の硬度及び透
磁率を示す。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均熱処理後またはそのまま線材
圧延した。また、耐銹性試験の評価のために、前記ビレ
ットを均熱処理後またはそのまま熱間圧延して熱延板と
し、さらに該熱延板から１ｍｍ厚さの冷延板を製造し
た。各特性の評価は下記の方法で行った。EXAMPLES Next, the superiority of the present invention will be specifically described with reference to Examples and Comparative Examples. Tables 1 and 2 (continued from Table 1) show the chemical compositions of the present invention and comparative examples, and Tables 3 and 4 (continued from Table 3) show the hardness after cold working and the hardness and magnetic permeability after aging treatment. Indicates. All of the test materials used in the normal refining process for stainless steel (vacuum or argon after melting in an electric furnace or converter)
The billet produced by continuous casting was melted and refined by refining by oxygen deoxidation treatment), and after the soaking, the billet was rolled into a wire rod. Further, for the evaluation of the rust resistance test, the billet was soaked or hot-rolled as it was to obtain a hot-rolled sheet, and a cold-rolled sheet having a thickness of 1 mm was produced from the hot-rolled sheet. Evaluation of each characteristic was performed by the following methods.
【００１５】（１）熱間加工性 １２５０℃加熱後１０００℃まで２０℃／ｓで冷却し、
１０００℃で６０ｓ間保定後５／ｓの歪み速度で引張破
断させ、その破断絞りで評価した。本発明材の絞り値は
６０％以上である。 （２）伸線加工後の硬度 ５．５ｍｍ線径の線材を６０％の伸線加工及び伸線加工
後５００℃にて１８００ｓの時効処理したもののビッカ
ース硬度を測定した。本発明材の硬度は６０％の冷間加
工時点でＨｖ４５０以上、時効処理後でＨｖ５５０以上
である。また、伸線加工後時効材の硬度の増加代は伸線
加工度の増加とともに大きくなるが、本発明材の時効に
よる硬度の増加代は６０％伸線加工後時効材でＨｖ５０
以上である。(1) Hot workability After heating at 1250 ° C., cooling to 1000 ° C. at 20 ° C./s,
After being held at 1000 ° C. for 60 s, tensile rupture was performed at a strain rate of 5 / s, and evaluation was made by the rupture drawing. The aperture value of the material of the present invention is 60% or more. (2) Hardness after wire drawing The wire rod having a diameter of 5.5 mm was drawn by 60%, and the Vickers hardness of the wire was aged for 1800 s at 500 ° C. after drawing. The hardness of the material of the present invention is Hv 450 or more at the time of 60% cold working, and Hv 550 or more after the aging treatment. Further, the increase margin of hardness of the aged material after wire drawing increases with the increase of the wire drawing degree, but the increase margin of hardness due to aging of the material of the present invention is Hv50 in the 60% aged material after wire drawing.
That is all.
【００１６】（３）冷間加工性 伸線加工性は、５．５ｍｍ線径の線材を９０％伸線した
場合の伸線破断の有無で評価した。本発明は冷間加工性
に優れており、８０％以上の伸線加工が可能である。 （４）磁性 ５．５ｍｍ線径の線材を３ｍｍ線径まで伸線加工（７
０．２％冷間加工）後、透磁率を測定した。本発明材の
透磁率は１．０５以下である。(3) Cold workability The wire drawability was evaluated by the presence or absence of wire breakage when 90% of a wire rod having a diameter of 5.5 mm was drawn. INDUSTRIAL APPLICABILITY The present invention is excellent in cold workability and is capable of 80% or more wire drawing. (4) Magnetism Wire drawing of 5.5 mm wire diameter to 3 mm wire diameter (7
After 0.2% cold working), the magnetic permeability was measured. The magnetic permeability of the material of the present invention is 1.05 or less.
【００１７】（５）耐銹性 ＪＩＳ−Ｚ ２３７１により１００ｈ試験後、面積法に
より評価した。本発明材のレイティングナンバは９．８
以上である。本発明例Ｎｏ．１、２と比較例Ｎｏ．２
１、２２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．２１は冷間加工後の硬度が本発明例に
比較して劣っている。また、Ｃが本発明の範囲を超える
Ｎｏ．２２は熱間加工性と冷間加工性に劣っており、本
発明の優位性が明らかである。(5) Rust resistance After a 100-hour test according to JIS-Z 2371, it was evaluated by the area method. The rating number of the material of the present invention is 9.8.
That is all. Inventive Example No. 1 and 2 and Comparative Example No. Two
Nos. 1 and 22 are for investigating the influence of C. No. C in which C is less than the range of the present invention. No. 21 is inferior in hardness after cold working to the inventive examples. In addition, No. where C exceeds the range of the present invention. No. 22 is inferior in hot workability and cold workability, and the superiority of the present invention is clear.
【００１８】本発明例Ｎｏ．３、４と比較例Ｎｏ．２
３、２４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．２３は冷間加工後の延性が本発明
例に比較して劣っている。また、Ｓｉが本発明の範囲を
超えるＮｏ．２４は熱間加工性及び冷間加工性に劣って
おり、本発明の優位性が明らかである。本発明例Ｎｏ．
５、６と比較例Ｎｏ．２５、２６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．２５は冷
間加工後の強度が本発明例に比較して劣っている。ま
た、Ｍｎが本発明の範囲を超えるＮｏ．２６は熱間加工
性及び冷間加工性に劣っており、本発明の優位性が明ら
かである。Inventive Example No. 3 and 4 and Comparative Example No. Two
Nos. 3 and 24 are for investigating the influence of Si. No. in which Si is less than the range of the present invention. No. 23 is inferior in ductility after cold working as compared with the inventive examples. In addition, No. in which Si exceeds the range of the present invention. No. 24 is inferior in hot workability and cold workability, and the superiority of the present invention is clear. Inventive Example No.
5 and 6 and Comparative Example No. Nos. 25 and 26 are for investigating the influence of Mn. No. in which Mn is less than the range of the present invention. No. 25 is inferior in strength after cold working to the inventive examples. Moreover, Mn in which Mn exceeds the range of the present invention. No. 26 is inferior in hot workability and cold workability, and the superiority of the present invention is clear.
【００１９】本発明例Ｎｏ．７、８と比較例Ｎｏ．２
７、２８はＰの影響を調査したものである。Ｐが本発明
範囲未満のＮｏ．２７は伸線加工後及び時効後の硬度が
低い。Ｐが本発明の範囲を超えるＮｏ．２８は熱間加工
性及び伸線性が劣っており、本発明の優位性が明らかで
ある。本発明例Ｎｏ．９、１０と比較例Ｎｏ．２９、３
０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．２９は熱間加工性及び冷間加工性が本発
明例に比較して劣っている。また、Ｎｉが本発明の範囲
を超えるＮｏ．３０は耐銹性が劣っており、本発明の優
位性が明らかである。Inventive Example No. 7 and 8 and Comparative Example No. Two
Nos. 7 and 28 are for investigating the influence of P. No. P in which P is less than the range of the present invention. No. 27 has low hardness after wire drawing and after aging. No. P in which P exceeds the range of the present invention. No. 28 is inferior in hot workability and wire drawability, and the superiority of the present invention is clear. Inventive Example No. 9, 10 and Comparative Example No. 29, 3
0 is an investigation of the effect of Ni. Ni whose Ni content is less than the range of the present invention. No. 29 is inferior in hot workability and cold workability to the inventive examples. In addition, No. in which Ni exceeds the range of the present invention. No. 30 is inferior in rust resistance, and the superiority of the present invention is clear.
【００２０】本発明例Ｎｏ．１１、１２と比較例Ｎｏ．
３１、３２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．３１は耐銹性が本発明例に比較
して劣っている。また、Ｃｒが本発明の範囲を超えるＮ
ｏ．３２は熱間加工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。本発明例Ｎｏ．１３、１
４と比較例Ｎｏ．３３、３４はＭｏの影響を調査したも
のである。Ｍｏが本発明範囲未満のＮｏ．３３は冷間加
工後及び時効後の硬度及び耐銹性が本発明例に比較して
劣っている。また、Ｍｏが本発明の範囲を超えるＮｏ．
３４は熱間加工性と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。Inventive Example No. 11 and 12 and Comparative Example No.
Reference numerals 31 and 32 are for investigating the influence of Cr. Cr with Cr less than the present invention range. No. 31 is inferior in rust resistance to the inventive examples. In addition, Cr exceeds N in the range of the present invention.
o. No. 32 is inferior in hot workability and cold workability, and the superiority of the present invention is clear. Inventive Example No. 13, 1
4 and Comparative Example No. 33 and 34 are for investigating the influence of Mo. No. in which Mo is less than the range of the present invention. No. 33 is inferior to the inventive examples in hardness and rust resistance after cold working and after aging. Moreover, No. in which Mo exceeds the range of the present invention.
34 is inferior in hot workability and cold workability, and the superiority of the present invention is clear.
【００２１】本発明例Ｎｏ．１５と比較例Ｎｏ．３５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．３５は冷間加工後及び時効後の硬度が劣
っており、本発明の優位性が明らかである。本発明例Ｎ
ｏ．１６、１７と比較例Ｎｏ．３６、３７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．３６
は冷間加工後及び時効後の硬度が本発明例に比較して劣
っている。Ｎが本発明の範囲を超えるＮｏ．３７は鋳造
したビレットに気泡の発生が認められる。また、Ｎｏ．
３７は熱間加工性と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。Inventive Example No. 15 and Comparative Example No. Reference numeral 35 is an investigation of the influence of Cu. No. where Cu exceeds the range of the present invention. No. 35 is inferior in hardness after cold working and after aging, and the superiority of the present invention is clear. Invention Example N
o. 16, 17 and Comparative Example No. 36 and 37 are for investigating the influence of N. N. where N is less than the range of the present invention. 36
Is inferior in hardness after cold working and after aging as compared with the inventive examples. No. N in which N exceeds the range of the present invention. In No. 37, bubbles were observed in the cast billet. In addition, No.
37 is inferior in hot workability and cold workability, and the superiority of the present invention is clear.
【００２２】本発明例Ｎｏ．１８と比較例Ｎｏ．３８は
Ａｌの影響を調査したものである。Ａｌが本発明範囲を
超えるＮｏ．３８は熱間加工性と冷間加工性が本発明例
に比較して劣っており、本発明の優位性が明らかであ
る。本発明例Ｎｏ．１９、２０と比較例Ｎｏ．３９、４
０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．３９は
伸線後及び時効後の硬度が本発明例に比較して劣ってい
る。全ての元素が本発明の上限を超えるＮｏ．４０は熱
間加工性、冷間加工性が劣っている。また、α値が本発
明範囲を超えるため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. 18 and Comparative Example No. 38 is a result of investigating the influence of Al. No. 1 in which Al exceeds the range of the present invention. No. 38 is inferior in hot workability and cold workability to the examples of the present invention, and the superiority of the present invention is clear. Inventive Example No. 19, 20 and Comparative Example No. 39, 4
0 is the result of investigating the influence of the lower limit and the upper limit of all elements of the present invention. All elements are No. below the lower limit of the present invention. In No. 39, the hardness after wire drawing and after aging is inferior to the inventive examples. No. in which all elements exceed the upper limit of the present invention. 40 is inferior in hot workability and cold workability. Further, since the α value exceeds the range of the present invention, the magnetic permeability is inferior, and the superiority of the present invention is clear.
【００２３】比較例Ｎｏ．４１、４２はαの値のみが本
発明の上限を超えるもので、熱間加工性、冷間加工性及
び透磁率が劣っており、本発明の優位性が明らかであ
る。本発明例Ｎｏ．１９材を用い、６０％伸線加工後の
時効温度と時間の硬度に及ぼす影響を調査した結果を表
５に、また本発明例Ｎｏ．２０材を用いて同様の調査を
行った結果を表６に示す。Comparative Example No. 41 and 42 are those in which only the value of α exceeds the upper limit of the present invention, and the hot workability, cold workability and magnetic permeability are inferior, and the superiority of the present invention is clear. Inventive Example No. Table 5 shows the results of an examination of the effects of the aging temperature and time on the hardness after 60% wire drawing using No. 19 material, and the invention example No. Table 6 shows the results of the same investigation using 20 materials.
【００２４】Ｎｏ．４３〜Ｎｏ．４６及びＮｏ．５５〜
Ｎｏ．５８は本発明範囲の時効条件にある。Ｎｏ．４７
〜Ｎｏ．５４及びＮｏ．５９〜６６は時効条件が本発明
範囲外にある比較材である。時効温度及び時間が本発明
範囲の下限未満及び上限を超えるいずれの場合も、時効
による硬化代が本発明材に比較して小さく、本発明の優
位性が明らかである。No. 43-No. 46 and No. 55-
No. 58 is an aging condition within the scope of the present invention. No. 47
~ No. 54 and No. 54. 59 to 66 are comparative materials whose aging conditions are outside the scope of the present invention. In both cases where the aging temperature and time are below the lower limit and above the upper limit of the present invention range, the curing margin due to aging is smaller than that of the present invention material, and the superiority of the present invention is clear.
【００２５】[0025]
【表１】 [Table 1]
【００２６】[0026]
【表２】 [Table 2]
【００２７】[0027]
【表３】 [Table 3]
【００２８】[0028]
【表４】 [Table 4]
【００２９】[0029]
【表５】 [Table 5]
【００３０】[0030]
【表６】 [Table 6]
【００３１】[0031]
【発明の効果】上述のように、本発明によれば、高硬度
と非磁性を両立させる課題を解決し、冷間加工後に高強
度と非磁性をもつ時効型高硬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。As described above, according to the present invention, an aging type high hardness non-magnetic stainless steel wire rod having high strength and non-magnetic property after cold working is solved by solving the problem of achieving both high hardness and non-magnetic property. It can be supplied at a low cost, and has industrially effective effects.
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Front page continuation (72) Inventor Wataru Murata 3434 Shimada, Hikari City, Yamaguchi Prefecture Nippon Steel Works Hikari Steel Works Ltd.
Claims (4)
ことを特徴とする高強度非磁性ステンレス鋼。 α＝１．６×Ｃｒ＋０．７７×Ｓｉ＋１．９４×Ｍｏ＋
０．０１２８×〔Ｍｎ〕2−０．１１×Ｍｎ−Ｎｉ−２
４．５×Ｃ−１８．４×Ｎ−２０．６…１式1. By weight%, C: 0.03 to 0.12% Si: 0.05 to 1.0% Mn: 10.0 to 17.0% P: 0.04 to 0.10% Ni : 0.5 to 6.0% Cr: 16.0 to 19.5% Mo: 0.5 to 2.5% N: 0.25 to 0.34% Al: 0.001 to 0.1% A high-strength non-magnetic stainless steel containing and having a value of α of 0 or less defined by the formula 1. α = 1.6 × Cr + 0.77 × Si + 1.94 × Mo +
0.0128 x [Mn] 2 -0.11 x Mn-Ni-2
4.5 x C-18.4 x N-20.6 ... 1 formula
とを特徴とする請求項１記載の高強度非磁性ステンレス
鋼。2. The high-strength non-magnetic stainless steel according to claim 1, further containing 2.0% or less of Cu.
つ透磁率が１．０５以下であることを特徴とする請求項
１または２記載の高強度非磁性ステンレス鋼。3. The high-strength non-magnetic stainless steel according to claim 1, which has a Vickers hardness of 550 or more and a magnetic permeability of 1.05 or less.
２０％以上９０％以下の加工率で冷間加工し、 続いて時効処理温度〔Ｔ〕（℃）と時効時間〔Ｈ〕（ｍ
ｉｎ）の関係において、 ５００−８５×ｌｏｇＨ ≦Ｔ≦６００−２５×ｌｏｇ
Ｈ １≦Ｈ≦１２０ の範囲の時効処理を施すことを特徴とする高強度非磁性
ステンレス鋼の製造方法。4. The stainless steel according to claim 1 or 2 is cold worked at a working rate of 20% or more and 90% or less, and subsequently, an aging temperature [T] (° C.) and an aging time [H] (m.
in), 500-85 × log H ≦ T ≦ 600-25 × log
A method for producing a high-strength non-magnetic stainless steel, which comprises subjecting an aging treatment within a range of H 1 ≦ H ≦ 120.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2152993A JPH06235049A (en) | 1993-02-09 | 1993-02-09 | High strength nonmagnetic stainless steel and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2152993A JPH06235049A (en) | 1993-02-09 | 1993-02-09 | High strength nonmagnetic stainless steel and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH06235049A true JPH06235049A (en) | 1994-08-23 |
Family
ID=12057490
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2152993A Withdrawn JPH06235049A (en) | 1993-02-09 | 1993-02-09 | High strength nonmagnetic stainless steel and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH06235049A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999023267A1 (en) * | 1997-11-05 | 1999-05-14 | Jessop Saville Limited | Non-magnetic corrosion resistant high strength steels |
| WO2008099336A1 (en) * | 2007-02-12 | 2008-08-21 | Thyssenkrupp Acciali Speciali Terni S.P.A. | Austenitic stainless steel |
| WO2014050943A1 (en) | 2012-09-27 | 2014-04-03 | 新日鐵住金ステンレス株式会社 | Super non-magnetic soft stainless steel wire material having excellent cold workability and corrosion resistance, method for manufacturing same, steel wire, steel wire coil, and method for manufacturing same |
| WO2017058456A1 (en) * | 2015-09-29 | 2017-04-06 | Exxonmobil Research And Engineering Company | Corrosion and cracking resistant high manganese austenitic steels containing passivating elements |
| CN107190214A (en) * | 2017-06-10 | 2017-09-22 | 深圳市富鹏达金属材料有限公司 | Steel alloy |
| CN107723641A (en) * | 2017-09-12 | 2018-02-23 | 广东坚朗五金制品股份有限公司 | The hot-dipping method of corrosion-resistant coating |
-
1993
- 1993-02-09 JP JP2152993A patent/JPH06235049A/en not_active Withdrawn
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999023267A1 (en) * | 1997-11-05 | 1999-05-14 | Jessop Saville Limited | Non-magnetic corrosion resistant high strength steels |
| WO2008099336A1 (en) * | 2007-02-12 | 2008-08-21 | Thyssenkrupp Acciali Speciali Terni S.P.A. | Austenitic stainless steel |
| WO2014050943A1 (en) | 2012-09-27 | 2014-04-03 | 新日鐵住金ステンレス株式会社 | Super non-magnetic soft stainless steel wire material having excellent cold workability and corrosion resistance, method for manufacturing same, steel wire, steel wire coil, and method for manufacturing same |
| KR20150044963A (en) | 2012-09-27 | 2015-04-27 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | Super non-magnetic soft stainless steel wire material having excellent cold workability and corrosion resistance, method for manufacturing same, steel wire, steel wire coil, and method for manufacturing same |
| US9863016B2 (en) | 2012-09-27 | 2018-01-09 | Nippon Steel & Sumikin Stainless Steel Corporation | Super non-magnetic soft stainless steel wire material having excellent cold workability and corrosion resistance, method for manufacturing same, steel wire, steel wire coil, and method for manufacturing same |
| WO2017058456A1 (en) * | 2015-09-29 | 2017-04-06 | Exxonmobil Research And Engineering Company | Corrosion and cracking resistant high manganese austenitic steels containing passivating elements |
| CN108026624A (en) * | 2015-09-29 | 2018-05-11 | 埃克森美孚研究工程公司 | Corrosion-resistant and cracking resistance high Mn austenitic steel containing passivation element |
| CN107190214A (en) * | 2017-06-10 | 2017-09-22 | 深圳市富鹏达金属材料有限公司 | Steel alloy |
| CN113718183A (en) * | 2017-06-10 | 2021-11-30 | 深圳市富鹏达金属材料有限公司 | Non-magnetic alloy steel |
| CN107723641A (en) * | 2017-09-12 | 2018-02-23 | 广东坚朗五金制品股份有限公司 | The hot-dipping method of corrosion-resistant coating |
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