JPS60110848A - Nonmagnetic high hardness steel - Google Patents

Abstract

PURPOSE:To obtain the titled steel having high strength and hardness and showing stable nonmagnetism by providing a specified composition consisting of C, Si, Mn, Ni, Cr, B, Ti, Al, Nb and Fe. CONSTITUTION:This nonmagnetic high hardness steel consists of, by weight, <=0.05% C, <=2.0% Si, <=2.0% Mn, 20-30% Ni, 15-20% Cr, <=0.010% B, 2.5- 5.0% Ti, 0.1-1.0% Al, 0.2-2.0% Nb and the balance essentially Fe while satisfying an equation Ti+Al+Nb=4.0-7.0atm% or further contains one ore more among 0.001-0.020% Mg, 0.001-0.050% Zr, 0.001-0.020% Ca and 0.001-0.050% REM. The steel has high strength and hardness and shows stable nonmagnetism, and it is suitable for use as the material of parts requiring nonmagnetism, strength and wear resistance.

Description

【発明の詳細な説明】 （産業上の利用分野） この発明は、強瓜および硬度が大であってしかも安定し
て非磁性を示し、例えば、非磁性ばね。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention provides a material that has high strength and hardness, yet stably exhibits non-magnetic properties, such as a non-magnetic spring.

ＶＴＲ用シャフト、非磁性金型などの素材として利用す
ることができる非磁性高硬度鋼に関するものである。The present invention relates to non-magnetic high-hardness steel that can be used as a material for VTR shafts, non-magnetic molds, etc.

（従来技術） 従来、例えば非磁性が要求される部品としては、電算機
に組込まれるリレースイッチ用ばねやＶＴＲ用シャフト
などがあり、これらの素材としては５ＵＳ３０４やＢｅ
−Ｃｕ系合金などが使用されていた。(Prior art) Conventionally, for example, parts that require non-magnetic properties include springs for relay switches incorporated in computers and shafts for VTRs, and these materials include 5US304 and Be.
-Cu-based alloys were used.

しかしながら、例えば５ＵＳ３０４の場合には低加工度
の状ｙルでは良好な非磁性が得られるものの強度および
硬度が低いため、強度」三部品寸法を小さくすることが
できなかったり、表面の摩耗が勇しかったりするという
欠点を有していた。一方、ＳＵ’５３０４の加工度を高
めて強度および硬度を一１＝　’ｉｌさせた場合には非
磁性のものを得ることができなくなり、」＝述した非磁
性が要求される部品の累月としては適さなくなるという
問題点があった。他力、Ｂｅ−Ｃｕ系合金の場合には安
定した非磁性が得られると共にある程度の強度および硬
度を４１しているが、近年の各種製品の小型軽ＪＩｉ化
の黄求に伴って部品のより一層の小型化が心霊となり、
このためにはさらに強度の大きい非磁性高強度材料が要
求されると共に、Ｖ　Ｔ　Ｐ、用シャフトなとの場合−
には硬度をより一層高めて耐摩耗性をさらに向上させ、
高品質の画像を長期にわたって得られるように、上記の
非磁性高強度に加えて高硬度の要求か強まってきている
。However, in the case of 5US304, for example, although good non-magnetic properties can be obtained in low-machined shapes, the strength and hardness are low, so it is not possible to reduce the dimensions of the three parts, and surface wear is severe. It had the disadvantage of being scolded. On the other hand, if the strength and hardness of SU'5304 are increased by 11 = 'il, it becomes impossible to obtain a non-magnetic product. There was a problem that it became unsuitable as a. In the case of Be-Cu alloys, stable non-magnetism can be obtained, as well as a certain degree of strength and hardness. Further miniaturization becomes a ghost,
For this purpose, a non-magnetic high-strength material with even greater strength is required, and in the case of shafts for VTP,
The hardness has been further increased to further improve wear resistance,
In order to obtain high-quality images over a long period of time, there is an increasing demand for high hardness in addition to the above-mentioned non-magnetic high strength.

（発明の目的） こめ発明は、上述した従来の事情に着目してなされたも
ので、強度および硬度が大であってしかも安定して非磁
性を示し、非磁性ならびに強度や耐摩耗性等が要求され
る部品の素旧として好適に使用することができる非磁性
高硬度鋼を提供することを目的としている。(Object of the invention) The present invention was made by paying attention to the above-mentioned conventional circumstances, and it has high strength and hardness, stably exhibits non-magnetic properties, and has excellent non-magnetic properties, strength, wear resistance, etc. The object of the present invention is to provide a non-magnetic high-hardness steel that can be suitably used as a material for required parts.

（発明の構成） この発明による非磁性高硬度鋼は、Ｃ：　０．０５重量
％以下、Ｓｉ：２．０重量％以下、Ｍｎ：２゜０重量％
以下、Ｎｉ：２０〜３０重量％、Ｃｒ：１５〜２０重量
％、Ｂ：０．０１０重量％以下、Ｔｉ：２．５〜５．０
重量％、Ａ文：０．１〜１．０重量％、Ｎｂ：０．２〜
２．０重量％でかつ原子％に換算してＴｉ＋Ａ文＋Ｎｂ
＝４．０〜７．０原子％を満足し、さらに必要に応じて
、Ｍｇ：０．００１〜０．０２０重量％。(Structure of the Invention) The non-magnetic high hardness steel according to the present invention contains C: 0.05% by weight or less, Si: 2.0% by weight or less, Mn: 2°0% by weight.
Below, Ni: 20-30% by weight, Cr: 15-20% by weight, B: 0.010% by weight or less, Ti: 2.5-5.0
Weight%, A text: 0.1 to 1.0 weight%, Nb: 0.2 to
2.0% by weight and converted to atomic%: Ti+A+Nb
Mg: 0.001 to 0.020% by weight, if necessary.

Ｚｒ：０．ＯＯｌ　〜０．０５０重量％、Ｃａ：ｏ、ｏ
ｏｉ〜０．０２０重量％、ＲＥＭ　（Ｙを含む希土類元
素）：Ｏ，ＯＯ１〜０．０５０重量％のうちの１種また
は２種以上を含有し、残部実質的にＦｅよりなることを
特徴としている。Zr: 0. OOl ~0.050% by weight, Ca: o, o
oi ~ 0.020% by weight, REM (rare earth element containing Y): O, OO 1 to 0.050% by weight, and the remainder substantially consists of Fe. There is.

次に、この発明による非磁性高硬度鋼の成分範囲の限／
Ｊ＝理由について説明する。Next, the limits of the composition range of the non-magnetic high hardness steel according to the present invention/
J = Explain the reason.

Ｃ：０．０５爪量％以下 Ｃは強力なオーステナイト形成元素であり、安定な非磁
性鋼を得るのに重要な元素であるが、Ｔｉ、Ｎｂなとの
ような炭化物形成元素を多量に含む鋼では巨大炭化物を
形成しやすく、また多量に含有すると靭延性が低下する
ため０　、０５ｆｉ１％以下に限定した。C: 0.05% or less C is a strong austenite-forming element and is an important element for obtaining stable non-magnetic steel, but it also contains large amounts of carbide-forming elements such as Ti and Nb. In steel, giant carbides are likely to form, and if a large amount is contained, the toughness and ductility decreases, so the content was limited to 0.05fi1% or less.

Ｓｉ二２，０重厚−％以下 Ｓｉは溶解時の脱酸元素として有効であるほか１．ｊ、
Ｉ度を高める効果を有する元素であるが、多ｊＩｊに含
有すると熱間加工性や磁気特性を害するため２．Ｑ屯４
１％以下に限定した。Si 2 2,0 weight -% or lessSi is effective as a deoxidizing element during melting.1. j,
It is an element that has the effect of increasing the I degree, but if it is contained in a large amount, it impairs hot workability and magnetic properties.2. Qtun 4
Limited to 1% or less.

Ｍ　ｎ　：　２　、　Ｏ爪Ｆｉ！４％以下Ｍｎは溶解時
の脱酸元素として有効であるほか、安定し５たオーステ
ナイト組織すなわち安定な非磁性を得るための重要な元
素であるが、γ′相やδ相を析出することにより高い硬
度を得る強析出型合金では析出硬化能を害するため２．
０重量％以下に限定した。Mn: 2, O nail Fi! 4% or less Mn is effective as a deoxidizing element during melting, and is an important element for obtaining a stable austenitic structure, that is, stable nonmagnetism. 2. Strong precipitation type alloys that achieve high hardness impair precipitation hardening ability.
It was limited to 0% by weight or less.

Ｎｉ：２０〜３０重量％ ・Ｎｉは安定なオーステナイト組織、すなわち安定な非
磁性を得るだめの必須元素であり、磁性および加工硬化
能を制御するためには少なくとも２０重量％以上含有さ
せることが必要であるが、多量に含有させても前記性質
が比例的に増大しなくなるほか、経済的にも高価となる
ため３０重量％以下に限定した。Ni: 20 to 30% by weight Ni is an essential element for obtaining a stable austenite structure, that is, stable nonmagnetism, and it is necessary to contain at least 20% by weight to control magnetism and work hardening ability. However, even if it is contained in a large amount, the above-mentioned properties do not increase proportionally, and it is also economically expensive, so it is limited to 30% by weight or less.

Ｃｒ：１５〜２０重量％ Ｃｒは安定な非磁性ならびに良好な耐応力腐食割れ性お
よび腐食抵抗性を得るだめの改善効果が顕著な元素であ
り、このような効果を得るためには１５重遍％以上含有
させることが必要であるが、多量に含有すると靭延性の
劣下を導き、磁気特性にも悪影響を及ぼすので２０重量
％以下に限定した。Cr: 15-20% by weight Cr is an element that has a remarkable effect on improving stable non-magnetism and good stress corrosion cracking resistance and corrosion resistance. It is necessary to contain more than 20% by weight, but since containing a large amount leads to deterioration of toughness and ductility and has an adverse effect on magnetic properties, the content is limited to 20% by weight or less.

Ｂ：Ｏ，ＯＩＯ重星５以下 Ｂは粒界を強化し、靭延性の向上を助長する作用を有す
るほか、熱間加工性の改善に顕著な効果を有する元素で
あるが、多量に含イ１すると低融点硼化物が生成し、脱
化温度領域が広くなるため０　、　Ｏ１，０重遍５％以
下に限定した。B: O, OIO double star 5 or less B is an element that strengthens grain boundaries and helps improve toughness and ductility, and has a remarkable effect on improving hot workability. When 1, a low melting point boride is produced and the deoxidization temperature range becomes wide, so the 0, O1,0 weight distribution was limited to 5% or less.

Ｔｉ：２．５〜５．０重液％ Ａす二０．１〜１．０重量％ Ｎｂ：０．２〜２．０型部％ Ｔｉ　、Ａ文、Ｎｂは微細な析出物γ′相、δ相の析出
硬化をもたらす必須元素であり、十分な硬さを１１Ｉる
には各々Ｔ　ｉ　：　２　、５重量％以上、ＡＭ＝０．
１重量％以」二、Ｎｂ：０．２重量％以上含イ）させる
ことが必要であるが、多量に含有させると苫しく熱間加
工性を害するため、上記成分範囲に限定した。そして、
安定な非磁性と十分な硬度を１１ノ・ると共に製造性の
観点から、原子％換算でＴ　ｉ　＋　Ａ文＋Ｎｂ＝４．
０〜７．０原子％どすることが最も望ましい。Ti: 2.5 to 5.0% heavy liquid A2 0.1 to 1.0% by weight Nb: 0.2 to 2.0% by weight Ti, A, and Nb are fine precipitates γ' phase , is an essential element that brings about precipitation hardening of the δ phase, and in order to obtain sufficient hardness, T i :2, 5% by weight or more, AM=0.
Nb: It is necessary to contain 0.2% by weight or more (i) of 1% by weight or more, but if it is contained in a large amount it will be harsh and impair hot workability, so the component range was limited to the above. and,
From the viewpoint of manufacturability, as well as stable non-magnetism and sufficient hardness, T i + A + Nb = 4.
It is most desirable that the content be 0 to 7.0 at%.

Ｍｇ：Ｏ，ＯＯ１〜０．０２０重量１％Ｚｒ：０．ＯＯ
Ｉ〜０．０５０重量％ Ｃａ＋０．００１〜０．０２０重品％ ＲＥ重量％、００１〜０．．０５０重量％Ｍｇ、Ｚｒ、
Ｃａ、ＲＥＭ（Ｙを含む右土類元素）はいずれも強靭性
の改善に右動な元素であり、また熱間加工性を著しく向
」ニーさせる作用を有しているが、多部に含有させると
粒界脆化の傾向を強めるので、」二足の範囲内でこれら
の１種または２種以」二を惑星に応じて添加する。Mg: O, OO1-0.020 weight 1% Zr: 0. OO
I~0.050 wt% Ca+0.001~0.020 wt% RE wt%, 001~0. ．． 050% by weight Mg, Zr,
Both Ca and REM (right-earth elements including Y) are elements that are effective in improving toughness, and also have the effect of significantly improving hot workability. Since this will increase the tendency of grain boundary embrittlement, one or more of these may be added depending on the planet.

（実施例１） 第１表に示す成分の未発明鋼を真空誘導炉により溶製し
たのち造塊して３０ｋｇ鋼塊を製造し、鍛造および圧延
を行ってＪｌｆ、さ１　ｍｍ　、幅２０ｍｍの平板を製
造し、次いで、第２表に示す熱処理条件で各平板を固溶
化熱処理したのち６６０°０Ｘ１０ｈｒの条件で時効処
理し、次いで時効処理後の平板材から厚さＩＩＩＩＩｌ
ｌ、ｌＩＩＩｉｉｌｏｍｍ、長さ１００ｍｍの薄板状試
験片を採取した。(Example 1) An uninvented steel with the components shown in Table 1 was melted in a vacuum induction furnace and then ingot-formed to produce a 30 kg steel ingot, which was then forged and rolled to have a Jlf of 1 mm and a width of 20 mm. A flat plate was manufactured, and then each flat plate was subjected to solution heat treatment under the heat treatment conditions shown in Table 2, and then aged under the conditions of 660°0 x 10 hr, and then the thickness of the flat plate after aging was
A thin plate-shaped test piece with a length of 100 mm and a length of 100 mm was taken.

また、第１表に示す成分の鋼のうちＢ、Ｅの鋼塊に対し
て鍛造および圧延を行って厚さ５ｍｍ、幅２０＋ｎ＋ｎ
の平板を製造し、次いで、第２表に示す熱処理条件で各
平板を固溶化熱処理したのち８０％の冷間加工を施して
厚さｌ　ｍｓ　、幅２０ｍｍの平板としたのち、６６０
℃Ｘ１０ｈｒの条件で時効処理し、次いで時効処Ｊｌｌ
！後の平板材から厚さｉｎ＋石２幅１０ｍｍ、長さ１０
０闘の薄板状試験片を採取した。In addition, steel ingots B and E of the steel compositions shown in Table 1 were forged and rolled to a thickness of 5 mm and a width of 20+n+n.
Next, each plate was subjected to solution heat treatment under the heat treatment conditions shown in Table 2, and then subjected to 80% cold working to obtain a flat plate with a thickness of 1 ms and a width of 20 mm.
Aging treatment under the conditions of ℃×10hr, then aging treatment Jll
! Thickness in + stone 2 width 10 mm, length 10 from the next flat plate material
A thin plate-shaped test piece with zero resistance was taken.

一方、比較のために、同じく第１表に示す成分の市販合
金を用意し、５ｔＬＳ３０４およびＢｅ−Ｃｕ合金に対
しては厚さ１ｍ１１まで冷間圧延した後、第２表に示す
条件で固溶化熱処理を行い、次いで時効処理を行ったの
ち、時効処理後の平板材から厚さ１　ｍｍ　、　ＩＩＶ
ｌｉ　１０ｒｎｍ　、長さ１００ｍｍの薄板状試験片を
採取した６さらに、５ＵＳ６３１に対しても第２表に示
す条件で熱処理を施し、前記と同寸法の薄板状試験片を
製作した。On the other hand, for comparison, commercially available alloys with the same composition shown in Table 1 were prepared, and 5tLS304 and Be-Cu alloys were cold rolled to a thickness of 1 m11 and then solid solution treated under the conditions shown in Table 2. After heat treatment and then aging treatment, a thickness of 1 mm was obtained from the aged plate material, IIV
A thin plate-like test piece with a li of 10 rnm and a length of 100 mm was taken6.Furthermore, 5US631 was also heat-treated under the conditions shown in Table 2 to produce a thin-plate test piece with the same dimensions as above.

次いで、各試験ノ）−の０．２％耐力、引張強さ、硬さ
および透磁率を測定したところ、第３表に示す結果とな
った。なお、第３表に木印で示すものは、　ＪｉｉＪ記
したように固溶化熱処理後に室温において加工率８０％
の冷間加工を行い、その後時効硬化処理した場合を示し
ている。Next, the 0.2% proof stress, tensile strength, hardness, and magnetic permeability of each test were measured, and the results are shown in Table 3. In addition, those indicated with wooden stamps in Table 3 have a processing rate of 80% at room temperature after solution heat treatment, as noted in JiiJ.
This shows the case where cold working was performed and then age hardening treatment was performed.

第２表 第　３　表 表に示す結果より明らかなように、本発明鋼Ａ〜Ｆはい
ずれも強度および硬度が大であってしかも良好な非磁性
をもつものであり、Ｍｇ、Ｚｒ。As is clear from the results shown in Tables 2 and 3, the steels A to F of the present invention all have high strength and hardness, as well as good nonmagnetic properties.

Ｃａ　、ＲＥＭの１種以上を添加した場合には強靭性お
よび熱間加工性を一層改善できることがわかった。また
、冷間における加工度を高めた場合には、安定な非磁性
を十分に確保した上でさらに強度および硬度を著しく高
めることができた。It has been found that the toughness and hot workability can be further improved when one or more of Ca and REM is added. Furthermore, when the degree of cold working was increased, it was possible to significantly increase the strength and hardness while ensuring sufficient stable nonmagnetism.

これに対して、比較の５ＵＳ３０４では良好な非磁性が
得られるものの強度および硬度が劣り、例えばばねの高
応力化に対応できないと共に、ＶＴＲ用シャフト等に適
用した場合に耐摩耗性が劣るものである。また、５ＵＳ
８３１は強度および硬度に優れているものの十分な非磁
性が得られず、Ｂｅ−Ｃｕ合金は良好な非磁性を有して
いるものの強度および硬度は十分満足いくものではない
。さらに、５ＵＳ３０４の冷間における加工度を高めた
場合には加工によりマルテンサイト化するため所望の非
磁性が得られなくなる。On the other hand, the comparative 5US304 has good non-magnetic properties but is inferior in strength and hardness, and cannot cope with high stress in springs, for example, and has poor wear resistance when applied to shafts for VTRs, etc. be. Also, 5US
Although 831 has excellent strength and hardness, it does not have sufficient nonmagnetism, and although Be-Cu alloy has good nonmagnetism, its strength and hardness are not fully satisfactory. Furthermore, if the degree of cold working of 5US304 is increased, the desired non-magnetic properties cannot be obtained because the working results in martensite formation.

次に、第１表に示す供試材のうち本発明鋼Ａ。Next, among the test materials shown in Table 1, the invention steel A.

Ｄ、’Ｅおよび市販合金５ＵＳ３０４．Ｂｅ−Ｃｕ合金
から製作した前記薄板状試験片についてばね限界値を測
定したところ、第４表に示す結果どなった。D, 'E and commercial alloy 5US304. When the spring limit value was measured for the thin plate-shaped test piece made from the Be-Cu alloy, the results are shown in Table 4.

第　４　表 第４表に示すように、本発明鋼ではいずれも良好な値を
示しており、ばねの高応力化に対応でき、あるいはばね
の小型化を実現することも可能である。これに対して比
較の５ＵＳ３０４では第３表に示したように強度が著し
く低く、ばね限界値も小さな値であり、Ｂｅ−Ｃｕ合金
ではばねの高応力化や小型化に十分対応できないもので
あった。Table 4 As shown in Table 4, all of the steels of the present invention show good values, and are able to cope with higher stress in springs or to realize miniaturization of springs. On the other hand, the comparative 5US304 has extremely low strength and a small spring limit value, as shown in Table 3, and the Be-Cu alloy cannot sufficiently respond to high stress and miniaturization of the spring. Ta.

（実施例２） 第１表に示す本発明鋼のうちＢ、Ｃ，Ｆの成分の鋼を真
空誘導炉で溶製したのち造塊して３０ｋｇ鋼塊を製造し
、鍛造および圧延を行って直径１０１１ｆｆｌの棒材を
製造した。次いで、前記第２表に示す熱処理条件で各棒
材を固溶化熱処理したのち冷間引抜きを行って直径３ｍ
ｍの棒材とし、次いで、６６０℃Ｘ１０ｈｒの条件で時
効処理してＶＴＲ用シャフトを製作した。(Example 2) Among the steels of the present invention shown in Table 1, steels with components B, C, and F were melted in a vacuum induction furnace and then formed into ingots to produce a 30 kg steel ingot, which was then forged and rolled. A bar with a diameter of 1011 ffl was produced. Next, each bar was subjected to solution heat treatment under the heat treatment conditions shown in Table 2 above, and then cold drawn to a diameter of 3 m.
A shaft of VTR was produced by aging the bar material at 660° C. for 10 hours.

一方、比較のために同じく第１表に示す成分の市販合金
５ＵＳ３０４および５ＵＳ６３１を用意し、５ＵＳ３０
４に対しては冷間圧延したのち第２表に示す熱処理条件
で固溶化熱処理を行い、次いで時効処理を施して同じ＜
ＶＴＲ用シャフトを製作した。また、５ＵＳ６３１に対
しては同じく第２表に示す条件で熱処理を施すことによ
り、ＶＴＲ用シャフトを製作した。さらに、５ＵＳ３０
４については加工度を９０％まで高めたものについても
製作した。On the other hand, for comparison, commercially available alloys 5US304 and 5US631 having the same composition shown in Table 1 were prepared, and 5US30
4 was cold rolled, then subjected to solution heat treatment under the heat treatment conditions shown in Table 2, and then subjected to aging treatment.
We manufactured shafts for VTRs. Further, 5US631 was heat treated under the conditions shown in Table 2 to produce a VTR shaft. Furthermore, 5US30
Regarding No. 4, we also manufactured a version with a processing degree of up to 90%.

次いで、各ＶＴＲ用シャフトを実機テストに供し、テー
プ走行５００時間後の摩耗減量を測定すると共に、再生
された画質についても調べた。また、人工海水中で５０
時間浸漬して発錆の有無を調べた。この結果を第５表に
示す。Next, each VTR shaft was subjected to an actual machine test, and the wear loss after 500 hours of tape running was measured, and the reproduced image quality was also examined. In addition, 50% in artificial seawater
The samples were immersed for a period of time and examined for the presence or absence of rust. The results are shown in Table 5.

第５表 第５表に示すように、本発明鋼はいずれも摩耗減量が少
なく、ｌｉｗ腐食性も良好であって、ＶＴＲ用シャフト
の寿命延長を実現することが可能であり、画質も良好で
あるというすぐれた結果が得られた。Table 5 As shown in Table 5, all of the steels of the present invention have low wear loss, good LIW corrosion resistance, can extend the life of VTR shafts, and have good image quality. An excellent result was obtained.

これに対して、比較の５ＵＳ３０４では硬度が低いため
摩耗が多く、９０％加工を施して硬度を高めた場合には
画質が劣ると共に耐腐食性にも劣っており、また５ＵＳ
６３１の場合にも画質が劣ると共に耐腐食性にも劣ると
いう好ましくない結果となった。On the other hand, the comparative 5US304 suffers from a lot of wear due to its low hardness, and when the hardness is increased by 90% processing, the image quality is inferior and the corrosion resistance is also inferior.
In the case of 631 as well, the image quality was poor and the corrosion resistance was also poor, which were undesirable results.

（発明の効果） 以上説明してきたように、この発明による非磁性高硬度
鋼は、Ｃ：０．０５重量％以下、Ｓｊ：２．０重量％以
下、Ｍｎ：２．０重量％以下。(Effects of the Invention) As explained above, the nonmagnetic high hardness steel according to the present invention contains C: 0.05% by weight or less, Sj: 2.0% by weight or less, and Mn: 2.0% by weight or less.

Ｎ　＋　：　２０〜３０重量％、Ｃｒ：１５〜２０重量
％、Ｂ：０．０１０重量％以下、Ｔｉ：２．５〜５．０
重量％、ＡｆＬ：０．１〜１．０重量％、Ｎｂ：０．２
〜２．０重量％でかつ原子％に換算してＴ　ｉ　＋　Ａ
文＋Ｎｂ＝４．０〜７．０原子％を満足し、さらに必要
に応じて、Ｍｇ：０．００１〜０．０２０重都Ｘ。N+: 20-30% by weight, Cr: 15-20% by weight, B: 0.010% by weight or less, Ti: 2.5-5.0
Weight %, AfL: 0.1 to 1.0 weight %, Nb: 0.2
~2.0% by weight and converted to atomic% T i + A
Satisfies carbon + Nb = 4.0 to 7.0 atomic %, and if necessary, Mg: 0.001 to 0.020 Juto X.

Ｚｒ：０．００１−０．０５０ｉＪ１％、Ｃａ：０．０
０１〜０．０２０重量％、ＲＥＭ　（Ｙを含む希土類元
素）：０．００１〜０．０５０重量％のうちの１種また
は２種以上を含有し、残部実質的にＦｅよりなるもので
あるから、強度および硬度が大であってしかも安定して
良好な非磁性を示すものであり、非磁性が要求されると
同時に強度や耐摩耗性等が要求される部品の素材として
好適に使用することができ、例えば電算機等のリレース
イッチ用非磁性ばねの高応力化や小型化に十分対応する
ことができ、ＶＴＲ用シＶフトの強度増大、小型化およ
び耐摩耗性向上を実現することができ、非磁性金型の強
靭化による耐割れ性の向上および金型寿命の延長をはか
ることができるなど、著しくすぐれた効果をもたらすも
のである。Zr: 0.001-0.050iJ1%, Ca: 0.0
01 to 0.020% by weight, REM (rare earth element containing Y): 0.001 to 0.050% by weight, and the remainder substantially consists of Fe. , has high strength and hardness, and exhibits stable and good non-magnetism, and can be suitably used as a material for parts that require non-magnetism as well as strength, wear resistance, etc. For example, it can fully cope with the high stress and miniaturization of non-magnetic springs for relay switches in computers, etc., and can realize increased strength, miniaturization, and improved wear resistance of VTR shafts. It brings about remarkable effects such as improving the cracking resistance and extending the life of the mold by making the non-magnetic mold tougher.

特許出願人　大同特殊鋼株式会社Patent applicant: Daido Steel Co., Ltd.

Claims (1)

【特許請求の範囲】 （＋）Ｃ：０．０．５型部％以下、Ｓｉ　：２．Ｏ重Ｉ
Ａ％以下、Ｍｎ：２．０重量％以下、Ｎｉ　：　２０〜
３　Ｑ　型部％、Ｃｒ：１５〜２０重量％、Ｂ：０　、
０１　Ｃ）ｉｒ、（ｉｉ％以下、Ｔｉ：２．５〜５．０
ｒｒＩ′＋１１％、ＡｆＬ：　０　、　ｌ−１、０ｉ１
．％、Ｎｂ：０．２〜２．０重量％でかつＴｉ＋Ａ文＋
Ｎｂ＝４．０〜７．０原子％を満足し、残部実質的にＦ
ｅよりなることを特徴とする非磁性高硬度鋼。 （２）Ｃ：０．０５重型底以下、Ｓｔ　：２．Ｏ重Ｉ−
％以下、Ｍ　ｎ　：　２　、０重量％以下、Ｎｉ：２０
〜３０［ｉｌ　％、　Ｃｒ：１５〜２０　重ｆｆｉ二％
、Ｂ：Ｏ，ＯＩＯ爪量％以下、Ｔｉ：２．５〜５．０屯
４１％、Ａ文＝０．１〜１．０重量％、Ｎｂ：０．２〜
２．０重量％でかつＴ　ｉ　＋　Ａ文＋Ｎｂ＝４．０〜
７．０原子％を満足し、さらにＭｇ：０．ＯＯ１〜０．
０２０重量％。 Ｚｒ：０．００１〜０．０５０重量％、Ｃａ：Ｏ，ＯＯ
１〜０．０２０重量％、ＲＥＭ：ｏ、ｏｏｉ〜０．０５
０重量％のうちの１種または２種以上を含有し、残部実
質的にＦｅよりなることを特徴とする非磁性高硬度鋼。[Claims] (+)C: 0.0.5 mold part % or less, Si: 2. O Heavy I
A% or less, Mn: 2.0% by weight or less, Ni: 20~
3 Q mold part%, Cr: 15-20% by weight, B: 0,
01 C) ir, (ii% or less, Ti: 2.5 to 5.0
rrI'+11%, AfL: 0, l-1, 0i1
．． %, Nb: 0.2 to 2.0% by weight, and Ti + A pattern +
Satisfies Nb = 4.0 to 7.0 at%, and the remainder is substantially F.
A non-magnetic high hardness steel characterized by consisting of e. (2) C: 0.05 heavy bottom or less, St: 2. O Heavy I-
% or less, M n : 2, 0 weight % or less, Ni: 20
~30[il%, Cr:15-20 heavy ffi2%
, B: O, OIO nail amount % or less, Ti: 2.5 to 5.0 tons 41%, A text = 0.1 to 1.0 weight %, Nb: 0.2 to
2.0% by weight and T i + A sentence + Nb = 4.0~
7.0 atom %, and Mg: 0. OO1~0.
020% by weight. Zr: 0.001 to 0.050% by weight, Ca: O, OO
1 to 0.020% by weight, REM: o, ooi to 0.05
A non-magnetic high-hardness steel characterized by containing one or more of 0% by weight and the remainder substantially consisting of Fe.