JPS6293340A - High-manganese steel having high rolling contact fatigue characteristic - Google Patents
High-manganese steel having high rolling contact fatigue characteristicInfo
- Publication number
- JPS6293340A JPS6293340A JP23132485A JP23132485A JPS6293340A JP S6293340 A JPS6293340 A JP S6293340A JP 23132485 A JP23132485 A JP 23132485A JP 23132485 A JP23132485 A JP 23132485A JP S6293340 A JPS6293340 A JP S6293340A
- Authority
- JP
- Japan
- Prior art keywords
- heat treatment
- steel
- manganese steel
- less
- high manganese
- 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.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、特にころがり疲労特性にすぐれた高マンガン
鋼に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a high manganese steel particularly having excellent rolling fatigue properties.
従来、ころがり疲労が問題となる機械部品２例えば、歯
車、キルンのローラなどには、高周波焼入れ、浸炭、窒
化または溶射などの表面硬化処理を施すか、または、こ
のような表面硬化処理を施せない場合２例えば、コスト
的に考えて、ｆ、たは。Conventionally, mechanical parts where rolling fatigue is a problem 2 For example, gears, kiln rollers, etc., are either subjected to surface hardening treatments such as induction hardening, carburizing, nitriding, or thermal spraying, or cannot be subjected to such surface hardening treatments. Case 2 For example, considering cost, f, or.
形状、大きさが表面硬化処理を施すのに著しく不適当な
場合など、この部品は、ころがり疲労によるハクリが生
じた時点で取替えが必要な消耗品となる。If the shape or size of the part is extremely inappropriate for surface hardening treatment, this part becomes a consumable item that needs to be replaced when peeling occurs due to rolling fatigue.
しかし、ハクリが生じるたびに部品を取替えるのでは、
コストがかかる上に、ノ・クリに気すかずに機械を運転
していて事故となる場合も生ずる。However, replacing parts every time peeling occurs,
Not only is it costly, but accidents can also occur if the machine is operated without paying attention to the operating conditions.
また２表面硬化処理はコストがかかる上に２例えば、浸
炭の場合は粒界酸化、溶射の場合は、溶着金材と母材の
整合性が悪くノ・クリするなど、一般的に処理の安定性
に欠け、これに基因する事故が多い。さらに２表面硬化
処理の場合、摩耗、もしくは、それに類する原因で表面
硬化層が取りさられた場合、その効果は全くなくなって
し斗う。In addition, 2) surface hardening treatment is costly, and 2) for example, in the case of carburizing, grain boundary oxidation, and in the case of thermal spraying, the consistency between the welded metal and the base metal is poor, resulting in cracks, etc., and the process is generally unstable. Many accidents are caused by this. Furthermore, in the case of the second surface hardening treatment, if the surface hardening layer is removed due to wear or similar causes, the effect will be completely lost.
本発明の鋼は、１−、記の従来表面硬化処理の問題点を
解決し２表面？＋’ｌＪｉ化処理を施した鋼と同等、丑
たは、それ以上の高ころがり疲労特性を有するものであ
る。The steel of the present invention solves the problems of conventional surface hardening treatment as described in 1- and 2. It has high rolling fatigue properties equivalent to, or even better than, steel subjected to +'lJi treatment.
すなわち、高マンガン鋼は９通常Ｈｖ ２００〜２５０
程度の硬さを有するが、衝撃力などの子′１荷が加わる
と、その部分の表面層が硬くなるという特性を持ってい
る。このため９表面硬化処理を施さなくとも、使用中に
容易に安定した表面硬化層を得ることができるだけでな
く、摩耗もり、＜は。That is, high manganese steel is 9 normal Hv 200-250
It has a certain degree of hardness, but when a load such as an impact force is applied, the surface layer of that part becomes hard. Therefore, even without surface hardening treatment, it is possible not only to easily obtain a surface hardened layer that is stable during use, but also to prevent wear and tear.
それに類する原因で表向硬化層が取りさられても。Even if the surface hardening layer is removed due to similar reasons.
さらにその下の層が硬化するという利点を持っている。Furthermore, it has the advantage that the underlying layer is hardened.
さらに、高マンガン鋼は表面硬化処理を施した鋼に比べ
てはるかに安価であり、形状、大きさの制限がない。Furthermore, high manganese steel is much cheaper than surface-hardened steel, and there are no restrictions on shape or size.
しかし２例えば浸炭の場合１表面硬化層はＨｖ７００〜
８００であるのに比較して、ころがり疲労が生じるよう
な使用状態の場合、すなわち。However, 2 For example, in the case of carburizing, 1 the surface hardening layer is Hv700 ~
800, when the condition of use is such that rolling fatigue occurs, that is.
応力はかかっているが衝撃力の加わらないような使用状
態の場合、後記する第１表に示すように。In the case of usage conditions where stress is applied but no impact force is applied, as shown in Table 1 below.
高マンガン鋼の表面層はＨｖ４５０〜５００程度にしか
ならず、この表面層の硬さから高マンガン鋼が表面硬化
処理を施した鋼と同等または、それ以上の高ころが９疲
労特性を有することを推測できないため、従来、高マン
ガン鋼は、ころがシ疲労が問題と々る部品に使用されて
いなかった。The surface layer of high manganese steel is only about 450 to 500 Hv, and from the hardness of this surface layer, it is estimated that high manganese steel has 9 fatigue characteristics, which is equivalent to or higher than surface hardened steel. Therefore, high manganese steel has not been used in parts where roller fatigue is a problem.
〔問題点を解決するための手段および作用〕本発明にお
いては、これらの問題点を解決するために、高ころがシ
疲労特性を有する高マンガン鋼を得た。[Means and effects for solving the problems] In the present invention, in order to solve these problems, a high manganese steel having high rollers and fatigue characteristics was obtained.
本発明においては、高マンガン鋼を１重量％で。In the present invention, high manganese steel is used at 1% by weight.
Ｃ： ０．７−１．５％、 Ｓｉ： ０．８％以下、Ｍ
ｎ：１０〜１５チ、残部がＦｅおよび不可避的不純物か
らなる高ころがり疲労特性を有する高マンガン鋼とする
か、または２重量％で、 Ｏ： ０．７〜１．５チ、Ｓ
ｉ：０．８チ以下、Ｍｎ：１０−１５％で、これに、Ｎ
ｉ：５チ以下、ｃｒ：３ｔＩｂ以下、Ｃｕ：１．５％以
下、Ｍｏ：３チ以下、Ｖ：３％以下、および、Ｔｉ：２
％以下のうちの１種または２種以上を含有し、残部がＦ
ｅおよび不可避不純物からなる高ころがり疲労特性を有
する高マンガン鋼とした。C: 0.7-1.5%, Si: 0.8% or less, M
n: 10 to 15 inches, the balance being Fe and unavoidable impurities, high manganese steel with high rolling fatigue properties, or 2% by weight, O: 0.7 to 1.5 inches, S
i: 0.8 or less, Mn: 10-15%, and N
i: 5 or less, cr: 3tIb or less, Cu: 1.5% or less, Mo: 3 or less, V: 3% or less, and Ti: 2
% or less, and the remainder is F.
This is a high manganese steel with high rolling fatigue properties consisting of E and unavoidable impurities.
そして２本発明においては、これら成分の高マンガン鋼
を用い、高マンガン鋼を１０００〜１２００℃で溶体化
熱処理を行った後、急冷してオーステナイト単相を得９
次に、５００〜７００℃まで加熱し、ここで焼戻しして
パーライト化熱処理を行い、続いて、再加熱した後、９
５０〜１１００℃で再溶体化熱処理を行い、最後に急冷
するようにして、高ころがり疲労特性を有する高マンガ
ン鋼を得るようにした。2 In the present invention, high manganese steel having these components is used, and after solution heat treatment is performed on the high manganese steel at 1000 to 1200 °C, the high manganese steel is rapidly cooled to obtain an austenite single phase.
Next, it is heated to 500 to 700°C, tempered here and subjected to pearlite heat treatment, and then reheated,
A re-solution heat treatment was performed at 50 to 1100° C., followed by rapid cooling at the end to obtain a high manganese steel having high rolling fatigue properties.
あるいは、これら成分の高マンガン鋼を、 １０００〜
１２００’Ｃで溶体化熱処理を行った後、急冷してオー
ステナイト単相を得２次に５００〜６００℃まで加熱し
、ここで焼戻ししてパーライト化熱処理を行い、続いて
、４〜１００℃／ ｍｉｎで再加熱した後、８００〜９
５０℃で再溶体化熱処理を行い、最後に急冷するように
して、高ころがシ疲労特性を有する高マンガン鋼を得る
ようにした。Alternatively, high manganese steel with these components, 1000 ~
After performing solution heat treatment at 1200'C, it is rapidly cooled to obtain a single austenite phase, which is then heated to 500-600°C, tempered here and subjected to pearlitization heat treatment, followed by 4-100°C/ 800-9 after reheating at min.
A re-solution heat treatment was carried out at 50° C., followed by rapid cooling at the end to obtain a high manganese steel having high roller fatigue characteristics.
つぎに２本発明の高マンガン鋼において、成分組成を上
記の通りに限定した理由を説明する。Next, the reason why the component compositions of the two high manganese steels of the present invention are limited as described above will be explained.
なお、各成分組成は、すべて重量係であられす。In addition, all component compositions are based on weight.
（ａ） Ｃ、Ｍｎ
Ｃ、Ｍｎ成分は、基地組織のオーステナイトの安定性と
、加工硬化特性に影響を与え、０．７〜１．５％０．１
０〜１５％Ｍｎの組合せが最も安定したオーステナイト
と高い加工硬化特性を有する。(a) C, Mn C, Mn components influence the stability of austenite in the matrix structure and work hardening properties, and are 0.7 to 1.5% 0.1
The combination of 0-15% Mn has the most stable austenite and high work hardening properties.
したがって、Ｃは０．７−１．５ ％ 、 Ｍｎは１０
−１５係とした。Therefore, C is 0.7-1.5%, Mn is 10
-15 staff members.
（ｂ） ５ｊ−
８］は、湯流れを良くするため不可欠の成分であるが、
０．８％を越えて含有させても、その効果ｄ：飽和する
ことから、上限をＯ０８受と定めた。(b) 5j-8] is an essential component to improve the flow of hot water, but
Even if the content exceeds 0.8%, the effect d: saturates, so the upper limit was set as O08.
（ｃ） Ｎｊ
Ｎｉは、オーステナイトを安定にするため、溶接施行が
必要となる部品の場合に、炭化物析出抑制のため、添加
されるが、５％以上添加させても効果が飽和することか
ら、上限を５係と定めた。(c) Nj Ni is added to stabilize austenite and suppress carbide precipitation in parts that require welding, but the effect is saturated even when added in an amount of 5% or more. The upper limit was set at 5.
（ｄ、） Ｃ！ｒ 、 ＭＯ Ｏｒ、Ｍｏは、降伏点、硬さを増大させるため。(d,) C! r, MO Or and Mo increase yield point and hardness.
高い降伏点を必要とする部品の場合に添加されるが、Ｃ
ｒは３係以上、 Ｍｏは３係以上添加させブこ場合。It is added for parts that require a high yield point, but C
If r is added in a ratio of 3 or more, and Mo is added in a ratio of 3 or more.
熱処理がむずかしくなり、脆性傾向がみとめられるため
、上限をＯｒは２％ ｌ ＭＯは３％と定めた。Since heat treatment becomes difficult and a tendency towards brittleness is observed, the upper limits were set as 2% for Or and 3% for MO.
（ｅ）Ｃｕ
Ｏｒ添加高マンガン鋼にＯｕを添加すると靭性の増大に
有効であるため、特に靭性を必要とする部品の場合に添
加されるが、１．５％以上添加させても効果が飽和する
ことから、上限を１．５係と定めた。(e) Cu Or addition Adding O to high manganese steel is effective in increasing toughness, so it is added especially for parts that require toughness, but the effect is saturated even when added at 1.5% or more. Therefore, the upper limit was set at 1.5 units.
（ｆ）Ｖ、Ｔｊ
これらの成分には２強度全向上させる効果があるので、
高強度が要求される部品の場合に添加されるが、■は３
％以上、 Ｔｊは２係以上添加すると靭性が低下するプ
ヒめ、上限を■は３％、Ｔｉは２係と定めた。(f) V, Tj These components have the effect of improving both strengths, so
It is added for parts that require high strength, but ■ is 3
% or more, the toughness decreases if Tj is added in a ratio of 2 or more, so the upper limit was set as 3% for ■ and 2% for Ti.
なお２本発明の鋼は、必要に応じて、第１〜６図に示し
た様なＱ■、◎の６種類の熱処理を施す。Note that the steel of the present invention is subjected to six types of heat treatment, Q■ and ◎, as shown in FIGS. 1 to 6, if necessary.
本熱処理の詳細を以下に述べる。The details of this heat treatment will be described below.
■ １０００〜１１００℃で２時間加熱した後・水冷す
る。■ After heating at 1000-1100°C for 2 hours, cool with water.
■ 以下に示す熱処理を■→■→■または■→■の順番
で施す。■ Apply the heat treatment shown below in the order of ■→■→■ or ■→■.
■ １０００〜１２００℃に加熱した後、空冷または水
冷する。■ After heating to 1000-1200°C, cool with air or water.
■ ５００〜７００℃で１０時間以上加熱した後、空冷
する。■ After heating at 500 to 700°C for 10 hours or more, air cooling.
■ ９５０〜１１００℃に加熱した後、水冷する。■ After heating to 950-1100°C, cool with water.
◎ 以下に示す熱処理を■→■→■または■→■の順番
で施す。◎ Perform the heat treatment shown below in the order of ■→■→■ or ■→■.
■ １０００〜１２００℃に加熱した後、空冷または水
冷する。■ After heating to 1000-1200°C, cool with air or water.
■ ５００〜６００℃で１０時間以上加熱した後、空冷
する。■ After heating at 500 to 600°C for 10 hours or more, air cooling.
■ ８００〜９５０℃に加熱した後、水冷する。■ After heating to 800-950°C, cool with water.
上記熱処理条件■において、鋼の加熱温度を１０００〜
１１００℃としたのは、１ｏｏｏ℃以上の温度域で、高
マンガン鋼はオーステナイト単相となシ、これを水冷す
ることにより常温で安定なオーステナイト組織をイ↓Ｉ
ることかできるからである。さらに、上限を１１００℃
としプこのは、オーステナイト単相組織を？４）るため
に、それ以上の加熱は必要ないからである。Under the above heat treatment condition (■), the heating temperature of the steel is
The temperature range of 1100°C was set at 100°C or above, and since high manganese steel has a single austenite phase, by water cooling it, an austenite structure that is stable at room temperature is created.↓I
This is because it is possible. Furthermore, the upper limit is set to 1100℃.
Does this have an austenite single phase structure? 4), no further heating is necessary.
■の熱処理は結晶粒を微細化させる熱処理である。すな
わち、■の工程でオーステナイト単相組織を得た後、■
の工程で、最もパーライトの析出しやすい５００〜７０
０℃の温度域でパーライトを析出させ、■の工程のパー
ライトが固溶する過程で結晶粒の微細なオーステナイト
単相組織を得る。ただし、鋳放しの状態で、針状炭化物
が析出しておらず、パーライトのみが析出している場合
。The heat treatment (2) is a heat treatment that refines crystal grains. That is, after obtaining the austenite single-phase structure in the step (■),
In the process of 500 to 70, pearlite is most likely to precipitate.
Pearlite is precipitated in a temperature range of 0°C, and an austenite single-phase structure with fine crystal grains is obtained in the process of solid solution of pearlite in step (2). However, in the as-cast state, if no acicular carbides are precipitated and only pearlite is precipitated.
■の工程を省略しても良い。Step (2) may be omitted.
上記に示した様に、■→■→■もしくは■→■の熱処理
を施した鋼は、結晶粒が微細であるため。As shown above, steel subjected to heat treatment of ■→■→■ or ■→■ has fine crystal grains.
特に靭性が要求される場合、または、特に高いころがり
疲労特性を要求される場合に使用される。It is used when particularly toughness is required or when particularly high rolling fatigue properties are required.
すなわち、後述の実施例で説明するが、高マンガン鋼の
ころがり疲労試験の結果、鍛造品（結晶粒。That is, as will be explained in Examples below, as a result of a rolling fatigue test of high manganese steel, a forged product (crystal grain) was found.
数祁程度）よシ、優れたころがり疲労特性を示したが、
■の熱処理工程を施して結晶粒を微細化させた鋳造品は
、鍛造品とほぼ同程度のころがり疲労特性を示したから
である。Although it showed excellent rolling fatigue properties,
This is because the cast product whose crystal grains were made finer through the heat treatment step (2) exhibited rolling fatigue characteristics that were approximately the same as those of the forged product.
■の熱処理は、■の熱処理とほぼ同じであるが。The heat treatment in (2) is almost the same as the heat treatment in (2).
主に異なるところは■の工程での温度が若干具々っでい
ることである。この例では、■の工程でオーステナイト
基地に４球状の炭化物が分散した組織を得る。その際、
熱処理温度を８００〜９００℃で変化させ、必要に応じ
た球状の炭化物の分散量を得る。The main difference is that the temperature in step (2) is slightly different. In this example, in step (2), a structure in which four spherical carbides are dispersed in an austenite base is obtained. that time,
The heat treatment temperature is varied from 800 to 900°C to obtain the amount of spherical carbide dispersed as required.
ｊｉＪ開１１１ノロ２−ａＪ 二ｊ４υ（５；）本発明
鋼のころがシ疲労耐久限度を調べる目的で、第１表に組
成を示した鋼を、高周波溶解炉にて約１００Ｋｇ溶製し
た。このインゴットに、調香１．２についてはぞのま寸
■、■工程の熱処理を施し、調香６の試料については、
鍛造比１ｏで鍛造した後、■工程の熱処理を施した。試
験機は菌属式金属摩耗試験機を用い、第４，５図に示し
た試験片１を＋ Ｅｆｌｉｐ ９％＋ ０−ラの回転数
８００ｒｐｍで疲労耐久限度を調べた。試験片１として
はリング状のものを２個１組用いた。In order to investigate the fatigue durability limit of the rollers of the steel of the present invention, approximately 100 kg of steel having the composition shown in Table 1 was melted in a high frequency melting furnace. This ingot was subjected to the heat treatment of steps ■ and ■ for perfume 1.2, and for perfume 6,
After forging at a forging ratio of 1o, heat treatment in step (2) was performed. The fatigue durability limit of the test piece 1 shown in FIGS. 4 and 5 was examined at +Eflip 9% + 0-ra rotation speed of 800 rpm using a fungal metal wear tester. As the test piece 1, a set of two ring-shaped pieces was used.
その結果を第６図に示す。本発明鋼（調香１゜２．３）
は、従来鋼（調香４，５．６）と比べて著しく優れた疲
労耐久限度を示した。The results are shown in FIG. Inventive steel (fragrance 1°2.3)
showed a significantly superior fatigue durability limit compared to conventional steel (fragrance 4, 5.6).
さらに２本発明鋼の特徴は、鋳造品（調香２）でも熱処
理によって鍛造品（調香５）と同程度のころがり疲労耐
久限度をイ４Ｊることかできることである。すなわち、
調香ろの鍛造品は調香１の鋳造品と比べて約１．５倍の
疲労耐久限度を示すが、Ｂ工程の熱処理を鋳造品に施す
ことによって調香２の様に鍛造品と同程度の疲労耐久限
度を得ることができた。Furthermore, two features of the steel of the present invention are that even a cast product (Fragrance 2) can have a rolling fatigue durability limit comparable to that of a forged product (Fragrance 5) by heat treatment. That is,
The forged product of the perfumer has a fatigue durability limit that is about 1.5 times that of the cast product of the perfumer 1, but by applying the heat treatment in process B to the cast product, it can be made similar to the forged product like the perfumer 2. We were able to obtain a fatigue endurance limit of approximately 100%.
第１〜３図は、それぞれ本発明鋼に施した熱処理の異な
る実施例を示した図、第４，５図はころがり疲労試験に
供した試験片の形状を示しブこ正面図と側面図、第６図
はころがり疲労試験結果を示す接触応力線図である。
１・・・・試験片Figures 1 to 3 are diagrams showing different examples of heat treatment applied to the steel of the present invention, Figures 4 and 5 are front and side views showing the shape of the test piece subjected to the rolling fatigue test, respectively. FIG. 6 is a contact stress diagram showing the results of a rolling fatigue test. 1...Test piece
Claims (4)
％以下、Ｍｎ：１０〜１５％、残部がＦｅおよび不可避
的不純物からなる高ころがり疲労特性を有する高マンガ
ン鋼。(1) In weight%, C: 0.7-1.5%, Si: 0.8
% or less, Mn: 10 to 15%, the balance being Fe and unavoidable impurities. High manganese steel with high rolling fatigue properties.
％以下、Ｍｎ：１０〜１５％、さらに、Ｎｉ：５％以下
、Ｃｒ：３％以下、Ｃｕ：１．５％以下、Ｍｏ：３％以
下、Ｖ：３％以下、およびＴｉ：２％以下のうちの１種
または２種以上を含有し、残部がＦｅおよび不可避的不
純物からなる高ころがり疲労特性を有する高マンガン鋼
。(2) In weight%, C: 0.7-1.5%, Si: 0.8
% or less, Mn: 10 to 15%, furthermore, Ni: 5% or less, Cr: 3% or less, Cu: 1.5% or less, Mo: 3% or less, V: 3% or less, and Ti: 2% or less. A high manganese steel containing one or more of the above, with the remainder consisting of Fe and unavoidable impurities and having high rolling fatigue properties.
℃で溶体化熱処理を行った後、急冷してオーステナイト
単相を得、次に、５００〜７００℃まで加熱し、ここで
焼戻ししてパーライト化熱処理を行い、続いて、再加熱
した後、９５０〜１１００℃で再溶体化熱処理を行い、
最後に急冷するようにして高ころがり疲労特性を有する
高マンガン鋼を得るようにした特許請求の範囲第１項ま
たは第２項記載の高ころがり疲労特性を有する高マンガ
ン鋼。(3) High manganese steel with a specified composition of 1000 to 1200
After solution heat treatment at ℃, quenching to obtain austenite single phase, then heating to 500-700℃, tempering here to perform pearlitization heat treatment, and then reheating to 950℃. Perform re-solution heat treatment at ~1100°C,
The high manganese steel having high rolling fatigue properties according to claim 1 or 2, wherein the high manganese steel having high rolling fatigue properties is obtained by finally rapidly cooling the steel.
℃で溶体化熱処理を行った後、急冷してオーステナイト
単相を得、次に、５００〜６００℃まで加熱し、ここで
焼戻ししてパーライト化熱処理を行い、続いて、４〜１
００℃／ｍｉｎで再加熱した後、８００〜９５０℃で再
溶体化熱処理を行い、最後に急冷するようにして高ころ
がり疲労特性を有する高マンガン鋼を得るようにした特
許請求の範囲第１項または第２項記載の高ころがり疲労
特性を有する高マンガン鋼。(4) High manganese steel with a specified composition of 1000 to 1200
After solution heat treatment at ℃, quenching to obtain austenite single phase, heating to 500-600℃, tempering here and pearlitization heat treatment, followed by 4-1
Claim 1: After reheating at 00°C/min, re-solution heat treatment is performed at 800 to 950°C, and finally quenching to obtain a high manganese steel having high rolling fatigue properties. Or a high manganese steel having high rolling fatigue properties as described in item 2.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23132485A JPS6293340A (en) | 1985-10-18 | 1985-10-18 | High-manganese steel having high rolling contact fatigue characteristic |
| JP7347790A JPH02270937A (en) | 1985-10-18 | 1990-03-26 | High manganese steel having high rolling contact fatigue properties and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23132485A JPS6293340A (en) | 1985-10-18 | 1985-10-18 | High-manganese steel having high rolling contact fatigue characteristic |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7347790A Division JPH02270937A (en) | 1985-10-18 | 1990-03-26 | High manganese steel having high rolling contact fatigue properties and its manufacture |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6293340A true JPS6293340A (en) | 1987-04-28 |
| JPH0251972B2 JPH0251972B2 (en) | 1990-11-09 |
Family
ID=16921848
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23132485A Granted JPS6293340A (en) | 1985-10-18 | 1985-10-18 | High-manganese steel having high rolling contact fatigue characteristic |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6293340A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100463992C (en) * | 2007-06-12 | 2009-02-25 | 燕山大学 | Forged (rolled) abrasive austenic permanganic steel and its manufacture |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS586960A (en) * | 1981-07-03 | 1983-01-14 | Daido Steel Co Ltd | High manganese steel rail |
-
1985
- 1985-10-18 JP JP23132485A patent/JPS6293340A/en active Granted
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS586960A (en) * | 1981-07-03 | 1983-01-14 | Daido Steel Co Ltd | High manganese steel rail |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100463992C (en) * | 2007-06-12 | 2009-02-25 | 燕山大学 | Forged (rolled) abrasive austenic permanganic steel and its manufacture |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0251972B2 (en) | 1990-11-09 |
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