JPH0466616A - Method for toughening stainless steel wire - Google Patents
Method for toughening stainless steel wireInfo
- Publication number
- JPH0466616A JPH0466616A JP17887390A JP17887390A JPH0466616A JP H0466616 A JPH0466616 A JP H0466616A JP 17887390 A JP17887390 A JP 17887390A JP 17887390 A JP17887390 A JP 17887390A JP H0466616 A JPH0466616 A JP H0466616A
- Authority
- JP
- Japan
- Prior art keywords
- wire
- stainless steel
- wire drawing
- steel wire
- ferrite
- 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.)
- Pending
Links
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 17
- 238000000034 method Methods 0.000 title claims description 19
- 238000005491 wire drawing Methods 0.000 claims abstract description 31
- 238000010438 heat treatment Methods 0.000 claims abstract description 25
- 238000005496 tempering Methods 0.000 claims abstract description 17
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 13
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 12
- 238000011282 treatment Methods 0.000 claims abstract description 9
- 238000010791 quenching Methods 0.000 claims description 7
- 230000000171 quenching effect Effects 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 4
- 229910001105 martensitic stainless steel Inorganic materials 0.000 claims 1
- 238000005728 strengthening Methods 0.000 claims 1
- 239000010935 stainless steel Substances 0.000 abstract description 5
- 238000005260 corrosion Methods 0.000 abstract description 4
- 230000007797 corrosion Effects 0.000 abstract description 4
- 229910000734 martensite Inorganic materials 0.000 abstract description 4
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 238000001816 cooling Methods 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 238000000137 annealing Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000007781 pre-processing Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野コ
本発明は、耐食性、耐熱性を兼ね備え、広範囲な分野に
おいて利用価値の高い１３Ｃｒ系ステンレス鋼線の高強
靭化を図る方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a method for increasing the strength and toughness of a 13Cr stainless steel wire that has both corrosion resistance and heat resistance and is highly useful in a wide range of fields.
［従来の技術］
従来から用いられている耐食性に優れた高強度ステンレ
ス鋼線の代表的なものとしては、ＪＩＳＧ ４３０９に
示されているようにオーステナイト系の５ＵＳ３０４．
１３Ｃｒ系の５ＵＳ４１Ｇ軟質２号がある。[Prior Art] A typical high-strength stainless steel wire with excellent corrosion resistance that has been conventionally used is austenitic 5US304. as shown in JISG 4309.
There is a 13Cr-based 5US41G soft No. 2.
このうち後者は焼なまし、あるいはさらに軽度の伸線加
工を行なうもので、高強度化を目的として焼入れ、焼戻
し処理を施したり、Ｗｌｒｅ Ｊｏｕｒｎａｌ（Ｏｃｔ
ｏｂｅｒ、 １９７８．Ｐ４４〜Ｐ５１）に示されてい
るように、Ｎｏ等の添加により高温脆性を改善するとと
もに、焼入れ、焼戻し処理及び適度な伸線加工を行なう
場合もある。Of these, the latter involves annealing or even light wire drawing.In order to increase the strength, quenching and tempering are performed, and Wlre Journal (Oct.
Ober, 1978. As shown in P44 to P51), high-temperature brittleness is improved by adding No, etc., and quenching, tempering, and appropriate wire drawing are sometimes performed.
さらに最近では一層の高強靭化を図るために、焼鈍材に
断面減少率３５％以上の強挿線加工を施したり（特願平
光−８０３７２号）、オーステナイト及びフェライトの
二相化熱処理材に低温焼戻し処理と断面減少率５０％以
上の伸線加工を施す方法（特願平２−３４９１７号）な
ど、新技術の開発が進められている。Furthermore, recently, in order to achieve even higher toughness, annealed materials are subjected to forcible wire processing with a cross-section reduction rate of 35% or more (Patent Application Hirako-80372), and austenite and ferrite dual-phase heat-treated materials are processed at low temperatures. New technologies are being developed, such as a method of tempering and wire drawing with a reduction in area of 50% or more (Japanese Patent Application No. 34917/1999).
〔発明が解決しようとする課題］
しかし、前記オーステナイト系の５Ｕ５３０４は、高価
なＮＩを含むため、価格面で一層のコストダウンが望ま
れ、一方Ｍｌを含まない＋３Ｃｒ系のステンレス鋼は、
非常に焼入れ硬化性に優れているものの、Ｃｒ元素自体
、炭化物形成能が大きいため、母相内あるいは結晶粒界
にＣｒ炭化物が形成されやすく、このため前記従来の方
法では鋼線の強度を高めることはできても、靭性がＣｒ
炭化物の析出状態に大きく左右されるという問題があっ
た。これは特に価格の安い細径の高強度ステンレス鋼を
製造する場合に重要な問題となっている。[Problems to be Solved by the Invention] However, since the austenitic 5U5304 contains expensive NI, further cost reduction is desired in terms of price.On the other hand, +3Cr stainless steel that does not contain Ml
Although it has excellent quench hardenability, the Cr element itself has a large carbide-forming ability, so Cr carbides are likely to be formed within the matrix or at grain boundaries.For this reason, the conventional method described above increases the strength of the steel wire. However, the toughness is Cr
There was a problem in that it was greatly influenced by the state of carbide precipitation. This is a particularly important problem when producing low-cost, small-diameter, high-strength stainless steel.
［課題を解決するための手段］
従って本発明は上記の問題点を解決すべくなされたもの
で、従来以上の優れた靭性をもたせるために、母相の均
質、微細化、炭化物の微細化、均一分散化を目指したス
テンレス鋼線の強靭叱方−法を提供するものである。[Means for Solving the Problems] Therefore, the present invention has been made to solve the above problems, and in order to provide better toughness than before, the present invention has been made by making the matrix homogeneous, finer, finer carbides, This provides a method for toughening stainless steel wire, aiming at uniform dispersion.
即ち、本発明方法は、重量％でＣ＜０．１５％、 Ｃｒ
１１．５０〜１４．００％、 Ｎｏ０．６０〜！、２０
％、Ｐ＜０．０４％、Ｓ＜０．０３％を含有し、残部が
Ｆｅ及び不可避的不純物からなるマルテンサイト系ステ
ンレス鋼の熱間圧延線材を９５０〜１１５０℃に加熱、
急冷して完全焼入れ処理を施し、これに伸線加工を行な
い、次いでオーステナイト及びフェライト二相域温度に
加熱保持した後急冷して二相化熱処理を施し、さらに伸
線加工を行なった後焼戻し処理を施すことを特徴として
いる。That is, in the method of the present invention, C<0.15% by weight, Cr
11.50~14.00%, No0.60~! , 20
%, P < 0.04%, S < 0.03%, with the remainder consisting of Fe and unavoidable impurities, heated to 950 to 1150 ° C.
It is rapidly cooled and subjected to complete quenching treatment, then subjected to wire drawing, then heated and maintained at a temperature in the austenite and ferrite two-phase region, then rapidly cooled and subjected to two-phase heat treatment, further wire drawn, and then tempered. It is characterized by applying
又、上記の加工、熱処理を施した線材にさらに伸線加工
、特に断面減少率５０％以上の伸線加工を施すことが望
ましい。Further, it is desirable that the wire material subjected to the above-mentioned processing and heat treatment is further subjected to a wire drawing process, particularly a wire drawing process with a reduction in area of 50% or more.
さらに、前記二相化熱処理における温度を８７５〜９２
０℃、焼戻し温度を２００〜５００℃とすることが好ま
しい。Furthermore, the temperature in the two-phase heat treatment is set to 875 to 92
It is preferable to set the tempering temperature to 0°C and the tempering temperature to 200 to 500°C.
本発明に用いるステンレス鋼は、前記のような重量％の
組成であるが、そのうちＣ量は初期強度（軟化焼鈍時）
及び炭化物析出量とのバランス、すなわち強度があって
靭性も悪くない様に決定したものであり、Ｐ、Ｓ量は脆
化の一原因である粒界偏析を防止するために低くしたも
のである。又ＭＯ量を上記の範囲で添加しであるのは、
焼戻し脆性が１無添加材と比較して高温側でも発生し難
くするためである。The stainless steel used in the present invention has the above-mentioned composition by weight, of which the amount of C is the initial strength (at the time of softening annealing).
The amount of P and S was determined to be balanced with the amount of precipitated carbides, that is, to have strength and good toughness, and the amounts of P and S were set low to prevent grain boundary segregation, which is one of the causes of embrittlement. . Moreover, when the amount of MO is added within the above range,
This is to make the tempering brittleness less likely to occur even at high temperatures compared to the material without 1 additive.
さて、このような組成からなる熱間圧延線材をまず９５
０℃以上１１５０℃以下に加熱後、急冷する。これは不
均一に形成している炭化物の溶体化を図るため下限を９
５０℃、又結晶粒間に酸化物が形成されずかつ溶融の生
じないよう上限を１１５０℃としたもので、この処理に
より比較的均質なマルテンサイト組織を有する線材が得
られる。Now, first, a hot rolled wire rod with such a composition is heated to 95
After heating to 0°C or more and 1150°C or less, it is rapidly cooled. The lower limit was set to 9 to dissolve the carbides that are unevenly formed.
The temperature is 50°C, and the upper limit is set to 1150°C so that oxides are not formed between crystal grains and melting does not occur, and a wire rod having a relatively homogeneous martensitic structure can be obtained by this treatment.
次にこの線材に伸線加工と二相化熱処理を施こすが、こ
の伸線加工により変形組織を導入し、これに続く二相化
熱処理の際、微細あるいは薄板状の逆変態γ（オーステ
ナイト）を形成させ、これを再び冷却することによりフ
ェライト中に微細なマルテンサイトが均一に散在した混
合組織が得られるのである。又、二相化熱処理はオース
テナイト及びフェライト二相域温度に加熱保持した後、
急冷することにより行なわれるが、上記二相域温度につ
いて鋭意検討した結果８７５〜９２０℃とすることが好
ましいことがわかった。Next, this wire rod is subjected to wire drawing processing and two-phase heat treatment, but this wire drawing process introduces a deformed structure, and during the subsequent two-phase heat treatment, a fine or thin plate-like reverse transformation γ (austenite) is introduced. By forming this and cooling it again, a mixed structure in which fine martensite is uniformly scattered in ferrite can be obtained. In addition, in the two-phase heat treatment, after heating and holding at the temperature in the austenite and ferrite two-phase region,
This is carried out by rapid cooling, and as a result of intensive study on the temperature in the two-phase region, it was found that a temperature of 875 to 920°C is preferable.
さらに、このようにして得られた鋼線に伸線加工を施し
、その後低温焼戻し処理を行なう。上記のような二相化
熱処理により得られた鋼線は、焼入れによって残存する
内部応力のため不安定な状態にある。このため一般的に
は低温焼戻し処理が必要となるが、この処理では炭化物
の析出が避けられない。そこで伸線加工を施してから低
温焼戻しを行なえば、変形組織の導入による炭化物形成
場所の増加により、炭化物は微細でかつ均一に分散され
る。これによって得られる鋼線は、単に従来の焼入れ、
焼戻し処理を行なったものと比較してかなり高靭性に優
れている。尚、この焼戻し温度は目的強度に応じて２０
０〜５００℃とすることが好ましい。Further, the steel wire thus obtained is subjected to wire drawing, and then subjected to low temperature tempering treatment. The steel wire obtained by the above-described two-phase heat treatment is in an unstable state due to internal stress remaining due to quenching. For this reason, low-temperature tempering treatment is generally required, but precipitation of carbides is unavoidable in this treatment. Therefore, if low-temperature tempering is performed after wire drawing, the carbide formation locations will increase due to the introduction of deformed structure, and the carbides will be finely and uniformly dispersed. The steel wire obtained by this can be simply conventionally quenched,
It has significantly higher toughness than those that have been tempered. In addition, this tempering temperature is 20% depending on the target strength.
It is preferable to set it as 0-500 degreeC.
そして、このようにして得られた鋼線に対して断面減少
率５０％以上の伸線加工を施せば、非常に強度、靭性に
優れたステンレス鋼線が得られるのである。If the steel wire thus obtained is subjected to wire drawing with a reduction in area of 50% or more, a stainless steel wire with extremely high strength and toughness can be obtained.
［実施例コ 以下、本発明を実施例及び比較例により説明する。[Example code] The present invention will be explained below with reference to Examples and Comparative Examples.
重量％でＣＯ，０１１８％、 Ｃｒ１１．５０％、 Ｎ
ｏ１．０２％、 Ｐｏ、０４％、 ８０．０３％、残部
がＦｅ及び不可避的不純物の化学組成よりなるステンレ
ス鋼の熱間圧延線材に対して以下の本発明の実施を含む
■〜■の処理を施した線材の機械的性質を調べた。尚、
素線は５，５■曽であった。Weight% CO, 0118%, Cr11.50%, N
A hot rolled stainless steel wire rod having a chemical composition of O1.02%, Po, 04%, 80.03%, and the balance being Fe and unavoidable impurities is subjected to the following treatments of (1) to (3) including the implementation of the present invention. The mechanical properties of the wire rods were investigated. still,
The wire had a diameter of 5.5 ■.
■焼鈍（７５０℃加熱→徐冷）したものに断面減少率９
０％の伸線加工を施したもの。（比較例）０１０５０℃
に加熱後油冷し、５００℃焼戻しを行ない、断面減少率
９０％の伸線加工を施したもの。■ Cross-sectional reduction rate of 9 for annealed (750℃ heating → slow cooling)
0% wire drawing process. (Comparative example) 01050℃
After heating, oil-cooling, tempering at 500°C, and wire drawing with a reduction in area of 90%.
（比較例）
０１０５０℃に加熱後油冷し、断面減少率４０％の伸線
加工を施し、５００℃焼戻しを行ない、さらに断面減少
率９０％の伸線加工を施したもの。(Comparative example) After heating to 01050°C, oil-cooling, wire drawing with a reduction in area of 40%, tempering at 500°C, and drawing with a reduction in area of 90%.
（比較例）
０１０５０℃に加熱後油冷し、断面減少率５０％の伸線
加工を施し、５００℃焼戻しを行ない、さらに断面減少
率９０％の伸線加工を施したもの。(Comparative example) After heating to 01050°C, oil-cooling, wire drawing with a reduction in area of 50%, tempering at 500°C, and drawing with a reduction in area of 90%.
（比較例）
０１０５０℃に加熱後油冷し、断面減少率４０％の伸線
加工を施し、続けて８９５℃のオーステナイト及びフェ
ライト二相域温度に加熱保持し、油冷して５００℃焼戻
しを行ない、さらに断面減少率９０％の伸線加工を施し
たもの。（比較例）０１０５０℃に加熱後油冷し、断面
減少率４０％の伸線加工を施し、続けて８９５℃のオー
ステナイト及びフェライト二相域温度に加熱保持し、油
冷後断面減少率４０％の伸線加工を施し、さらに５００
℃焼戻しを行なって、断面減少率３０％の伸線加工を施
したもの。（実施例）
０１０５０℃に加熱後油冷し、断面減少率４０％の伸線
加工を施し、続けて８３５℃のオーステナイト及びフェ
ライト二相域温度に加熱保持し、油冷後断面減少率５０
％の伸線加工を施し、さらに５００℃焼戻しを行なって
、断面減少率９０％の伸線加工を施したもの。（実施例
）
０８９５℃のオーステナイト及びフェライト二相域温度
に加熱保持し、油冷後５００℃焼戻しを行なって、断面
減少率８０％の伸線加工を施したもの。（比較例）
０８９５℃のオーステナイト及びフェライト二相域温度
に加熱保持し、油冷後断面減少率４０％の伸線加工を施
し、その後５００’Ｃ焼戻しを行なって、さらに断面減
少率９０％の伸線加工を施したもの。（比較例）
以上■〜■で示した各別の熱処理後断面減少率を９０％
とする伸線加工によって得られた線材について、引張強
度及び絞り値を表１と第１図のグラフに示し、又該グラ
フには断面減少率３０％までの伸線加工を行った際の途
中段階（断面減少率１０．５０．８０％）における引張
強度及び絞り値も示した。これにより線材に対する前加
工による機械的性質への効果を評価できる。(Comparative example) After heating to 01050°C, oil-cooling, wire drawing with a cross-section reduction rate of 40%, followed by heating and holding at 895°C, a temperature in the austenite and ferrite two-phase region, oil-cooling, and tempering at 500°C. wire drawing process with a cross-section reduction rate of 90%. (Comparative example) After heating to 01050°C, oil cooling, wire drawing with a cross-section reduction rate of 40%, followed by heating and holding at 895°C, a temperature in the austenite and ferrite two-phase region, and after oil cooling, a cross-section reduction rate of 40%. wire drawing process, and further 500
Celsius tempered and wire drawn with a cross-section reduction rate of 30%. (Example) After being heated to 01050°C, it was cooled in oil and subjected to wire drawing with a reduction in area of 40%, and then heated and maintained at a temperature in the austenite and ferrite two-phase region of 835°C, and after cooling in oil, the reduction in area was 50%.
% wire drawing, further tempered at 500°C, and wire drawn with a cross-section reduction rate of 90%. (Example) The material was heated and maintained at a temperature in the austenite and ferrite two-phase region of 0895°C, cooled in oil, tempered at 500°C, and subjected to wire drawing with a cross-section reduction rate of 80%. (Comparative example) A wire was heated and maintained at a temperature in the austenite and ferrite two-phase region of 0895°C, and after oil cooling, a wire was drawn with a cross-section reduction rate of 40%, and then tempered at 500°C, and further wire-drawn with a cross-section reduction rate of 90%. Wire-drawn. (Comparative example) The cross-section reduction rate after each heat treatment shown in ■ to ■ above is 90%.
Table 1 and the graph in Figure 1 show the tensile strength and reduction of area of the wire rod obtained by the wire drawing process. The tensile strength and area of area at a stage (area reduction rate of 10.50.80%) are also shown. This makes it possible to evaluate the effect of pre-processing on the mechanical properties of the wire.
表 １
（注） 処理Ｎ１１１．２．５．８．９は従来材、同３
．４は比較材、同６．７は本発明開発材である。Table 1 (Note) Treatment N111.2.5.8.9 is conventional material, same 3
．． 4 is a comparative material, and 6.7 is a material developed in the present invention.
表１において、ｍ８．７は引張強度絞り値共に最も高い
値を示すものではないが、他の処理材が引張強度又は絞
り値の一方で特に低い値を示しているのに対し、本発明
開発材は両者共に比較的大きな値を示している。このよ
うに本発明方法により、強度、靭性共にバランスのとれ
た優れたステンレス鋼線が得られることが確認された。In Table 1, m8.7 does not show the highest value for both tensile strength and aperture value, but whereas other treated materials show particularly low values for either tensile strength or aperture value, the present invention developed Both materials show relatively large values. As described above, it was confirmed that the method of the present invention yields an excellent stainless steel wire with well-balanced strength and toughness.
又、Ｎ１６とＮ１７を比較してみると陽７が二相化熱処
理後の伸線加工における断面減少率を１０％上げている
にもかかわらず、第１図のグラフに示すように鬼６と機
械的性質は同等であり、Ｎ１１６でも十分な効果がある
ことが確認された。In addition, when comparing N16 and N17, even though Yo 7 has a 10% increase in cross-sectional area reduction rate during wire drawing after two-phase heat treatment, it is different from Oni 6 as shown in the graph in Figure 1. It was confirmed that the mechanical properties were the same and that N116 was also sufficiently effective.
［発明の効果コ
以上説明したように、本発明は特定組成、すなわち重量
％でＣ＜ ０．１５％、 Ｃｒ１１．５０〜１４．００
％、 Ｎｏ０．６０〜１．２０％、 Ｐ＜０．１５％
、Ｓ＜０．０３％を含有し、残部がＦｅ及び不可避的不
純物からなるステンレス鋼線に対して、詳細に説明した
複合熱処理（完全焼入れ、二相化熱処理及び焼戻し）と
伸線加工（完全焼入れ後及び二相化熱処理後）を行なう
ことによって、耐食性、耐熱性さらに高強靭性に優れた
ステンレス鋼を製造することができる。[Effects of the Invention] As explained above, the present invention has a specific composition, that is, C<0.15% by weight, Cr11.50 to 14.00.
%, No0.60-1.20%, P<0.15%
, S<0.03%, with the balance consisting of Fe and unavoidable impurities. After quenching and after two-phase heat treatment), stainless steel with excellent corrosion resistance, heat resistance, and high strength and toughness can be produced.
第１図は熱処理後の伸線加工において断面減少率を変化
させた場合における、本発明方法及びその他の方法によ
って製造された線材の引張強度及び絞り値を示すグラフ
である。FIG. 1 is a graph showing the tensile strength and reduction of area of wire rods produced by the method of the present invention and other methods when the area reduction rate is changed in wire drawing after heat treatment.
Claims (3)
．００％、Ｍｏ０．６０％〜１．２０％、Ｐ＜０．０４
％、Ｓ＜０．０３％を含有し、残部がＦｅ及び不可避的
不純物からなるマルテンサイト系ステンレス鋼の熱間圧
延線材を９５０〜１１５０℃に加熱、急冷して完全焼入
れ処理を施し、これに伸線加工を行ない、次いでオース
テナイト及びフェライト二相域温度に加熱保持した後急
冷して二相化熱処理を施し、さらに伸線加工を行なった
後焼戻し処理を施すことを特徴とするステンレス鋼線の
強靭化方法。(1) C<0.15% in weight%, Cr11.50-14
．． 00%, Mo0.60%-1.20%, P<0.04
%, S<0.03%, with the remainder consisting of Fe and unavoidable impurities, a hot rolled martensitic stainless steel wire rod is heated to 950 to 1150°C, rapidly cooled and subjected to complete quenching treatment. A stainless steel wire that is drawn, then heated and held at a temperature in the austenite and ferrite two-phase region, then rapidly cooled and subjected to a two-phase heat treatment, further drawn, and then tempered. Toughening method.
さらに伸線加工、望ましくは断面減少率５０％以上の伸
線加工を施したことを特徴とするステンレス鋼線の強靭
化方法。(2) A wire rod subjected to the toughening method described in claim (1),
A method for strengthening stainless steel wire, which further comprises subjecting it to wire drawing, preferably wire drawing with a reduction in area of 50% or more.
５〜９２０℃、焼戻し温度を２００〜５００℃とするこ
とを特徴とする請求項（１）記載のステンレス鋼線の強
靭化方法。(3) Austenite and ferrite two-phase region temperature is 87
The method for toughening stainless steel wire according to claim 1, characterized in that the tempering temperature is 5 to 920°C and the tempering temperature is 200 to 500°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17887390A JPH0466616A (en) | 1990-07-05 | 1990-07-05 | Method for toughening stainless steel wire |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17887390A JPH0466616A (en) | 1990-07-05 | 1990-07-05 | Method for toughening stainless steel wire |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0466616A true JPH0466616A (en) | 1992-03-03 |
Family
ID=16056189
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17887390A Pending JPH0466616A (en) | 1990-07-05 | 1990-07-05 | Method for toughening stainless steel wire |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0466616A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0975783A (en) * | 1995-09-14 | 1997-03-25 | Mitsubishi Kakoki Kaisha Ltd | Centrifugal machine cleaner |
| SE1950909A1 (en) * | 2019-07-31 | 2021-02-01 | Ferritico Ab | Duplex steel with improved embrittlement properties and method of producing such |
-
1990
- 1990-07-05 JP JP17887390A patent/JPH0466616A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0975783A (en) * | 1995-09-14 | 1997-03-25 | Mitsubishi Kakoki Kaisha Ltd | Centrifugal machine cleaner |
| SE1950909A1 (en) * | 2019-07-31 | 2021-02-01 | Ferritico Ab | Duplex steel with improved embrittlement properties and method of producing such |
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