JP2002060887A - Method for manufacturing high purity bearing steel - Google Patents
Method for manufacturing high purity bearing steelInfo
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- JP2002060887A JP2002060887A JP2000250147A JP2000250147A JP2002060887A JP 2002060887 A JP2002060887 A JP 2002060887A JP 2000250147 A JP2000250147 A JP 2000250147A JP 2000250147 A JP2000250147 A JP 2000250147A JP 2002060887 A JP2002060887 A JP 2002060887A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、Ｔｉの炭窒化物が
微細な状態で存在する超清浄軸受鋼の製造方法に関す
る。この超清浄軸受鋼は、とくに音響特性が改善されて
いる。The present invention relates to a method for producing an ultraclean bearing steel in which Ti carbonitrides are present in a fine state. This ultra-clean bearing steel has particularly improved acoustic properties.
【０００２】[0002]
【従来の技術】軸受鋼の用途のひとつであるミニチュア
ベアリング用ボールは、良好な音響特性をもつこと、す
なわち使用中に異音を発生しないことがしばしば要求さ
れる。異音の発生原因は微小な介在物の存在にあること
がわかったので、介在物がきわめて少ない超清浄軸受鋼
の製造が試みられている。BACKGROUND OF THE INVENTION Balls for miniature bearings, one of the uses of bearing steel, are often required to have good acoustic characteristics, that is, not to generate abnormal noise during use. Since it has been found that the cause of the abnormal noise is the presence of minute inclusions, production of ultra-clean bearing steel with extremely few inclusions has been attempted.
【０００３】音響特性に影響する介在物としては、アル
ミナ系（Ａｌ2Ｏ3）介在物、酸化物複合系（ＭｇＯ・Ａ
ｌ2Ｏ3・ＣａＯ）介在物およびチタン系（ＴｉＣ，Ｔｉ
Ｎ）介在物が知られていて、それぞれ含有量を低減する
ための努力がなされている。前二者に対しては、脱ガス
の強化、介在物の形態制御、連続鋳造における非汚染鋳
造技術の探求などがあり、後者に対しては、原料の吟味
に加え、脱Ｔｉと脱ガスによるＴｉＮ量の制御などがそ
れである。ＶＡＲ（真空アーク再溶解）、ＥＳＲ（エレ
クトロスラグ再溶解）あるいはトリプルメルトなどの特
殊な溶解法もあり、これらによれば、ほぼ所望の製品が
得られるが、コスト面での不利は免れないから、やはり
通常の溶解−精錬のプロセスにより超清浄軸受鋼を製造
することが望まれる。[0003] Inclusions that affect the acoustic characteristics include alumina (Al 2 O 3 ) inclusions and oxide composite (MgO · A) inclusions.
l 2 O 3 .CaO) inclusions and titanium-based (TiC, Ti
N) Inclusions are known and efforts have been made to reduce their content. For the former two, there are enhancement of degassing, control of inclusion morphology, search for non-contamination casting technology in continuous casting, etc. For the latter, in addition to examination of raw materials, Controlling the amount of TiN, etc. is such. There are also special melting methods such as VAR (vacuum arc remelting), ESR (electroslag remelting) or triple melt, which can provide almost the desired product, but inevitably suffer from disadvantages in cost. It is also desirable to produce ultra-clean bearing steel by a conventional melting-refining process.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、ミニチュア
ベアリング用ボールの音響特性にとって、酸化物系介在
物の量が低減されるに従いクローズアップされてきた、
Ｔｉ炭窒化物の粒子を微細にした、超清浄軸受鋼の製造
方法を提供することにある。SUMMARY OF THE INVENTION The present invention has been focused on the acoustic characteristics of balls for miniature bearings as the amount of oxide-based inclusions is reduced.
An object of the present invention is to provide a method for producing ultra-clean bearing steel in which Ti carbonitride particles are made fine.
【０００５】[0005]
【課題を解決するための手段】この目的を達成する本発
明の超清浄軸受鋼の製造方法は、Ｔｉの炭窒化物が微細
な状態で存在する超清浄軸受鋼を製造する方法であっ
て、軸受鋼に必要な合金成分を含有し、かつ、分塊圧延
に先立つ均熱温度においてＴｉＮが実質上固溶する限度
内に［％Ｔｉ］×［％Ｎ］の値を低減した合金組成をも
つ軸受鋼を、連続鋳造により鋳片に鋳造し、この鋳片
を、均熱温度としては固溶平衡温度以上の温度をえら
び、均熱時間としてはＴｉの拡散速度に基づいて決定さ
れる、ＴｉＮの再固溶のために粒子の径が減少するに足
りる時間をえらんだ均熱を施して、その後に分塊圧延お
よび後続の圧延を行なうことを特徴とする。According to the present invention, there is provided a method for producing an ultra-clean bearing steel, comprising the steps of: It has an alloy composition that contains the necessary alloy components for the bearing steel and that reduces the value of [% Ti] x [% N] within the limit where TiN substantially dissolves at the soaking temperature prior to slab rolling. The bearing steel is cast into a slab by continuous casting, and the slab is selected to have a temperature equal to or higher than the solid solution equilibrium temperature as the soaking temperature, and the soaking time is determined based on the diffusion rate of TiN. Is characterized by performing soaking for a period of time sufficient for reducing the particle diameter for re-solid solution of, followed by slab rolling and subsequent rolling.
【０００６】より具体的にいえば、上記の製造方法は、
Ｔｉ：１０ppm以下、好ましくは７ppm以下、Ｎ：５０pp
m以下、好ましくは３０ppm以下、の軸受け鋼の鋳片を、
１２００℃以上、好ましくは１２４０℃程度の温度に１
時間以上加熱する均熱処理を施すことにより、長さが
７．５μｍ以上のＴｉＮ粒子が実質上存在しないように
した超清浄軸受鋼の製造方法である。[0006] More specifically, the above-mentioned manufacturing method comprises:
Ti: 10 ppm or less, preferably 7 ppm or less, N: 50 pp
m or less, preferably 30 ppm or less, a slab of bearing steel,
1200 ° C. or higher, preferably about 1240 ° C.
This is a method for producing ultra-clean bearing steel in which TiN particles having a length of 7.5 μm or more are substantially absent by performing a soaking process of heating for at least one hour.
【０００７】[0007]
【発明の実施形態】Ｔｉ：１０ppm以下、Ｎ：５０ppm以
下の条件は、［％Ｔｉ］×［％Ｎ］の値で決定されるＴ
ｉＮ生成量を抑える上で、満たすべきものである。均熱
温度を１２００℃以上とするのは、代表的なＴｉ＝４pp
m、かつＮ＝３０ppmの条件において、ＴｉＮがこの温度
において固溶するからである。このことは、図１に示す
実験結果から証明された。DESCRIPTION OF THE PREFERRED EMBODIMENTS The condition of Ti: 10 ppm or less and N: 50 ppm or less is determined by the value of [% Ti] × [% N].
This must be satisfied in order to suppress the iN generation amount. It is typical that the soaking temperature is set to 1200 ° C. or more because Ti = 4 pp.
This is because, under the conditions of m and N = 30 ppm, TiN forms a solid solution at this temperature. This was proved from the experimental results shown in FIG.
【０００８】図１は、上記したＴｉ＝４ppm、かつＮ＝
３０ppmの鋳片の、１１８０℃または１２４０℃に各６
時間加熱したのちの、Ｔｉ系介在物の粒度別の分布を、
鋳造ままのものと比較したグラフであって、長さが７．
５μｍ以上のＴｉ系介在物（主体はＴｉ炭窒化物）粒子
が、１１８０℃の加熱ではほとんど改善されていない
（３１個→２７個）のに対し、１２４０℃の加熱により
顕著に減少した（２個）ことを示している。FIG. 1 shows that Ti = 4 ppm and N =
30 ppm slabs at 1180 ° C or 1240 ° C
After heating for hours, the distribution of Ti-based inclusions by particle size is
7 is a graph in comparison to an as-cast one, with a length of 7.
Although the Ti-based inclusions (mainly Ti carbonitride) particles of 5 μm or more were hardly improved by heating at 1180 ° C. (31 → 27), they were significantly reduced by heating at 1240 ° C. (2 ).
【０００９】各［％Ｔｉ］および［％Ｎ］に応じたＴｉ
Ｎ固溶温度の計算値の代表例を示せば、次のとおりであ
る。Ｔｉ（ppm） Ｎ（ppm） ＴｉＮ固溶温度（℃） ３ ３０ １２０７ ４ ２０ １２２４ ４ ３０ １２４８ ４ ５０ １２８１ ４ ６０ １２９３ ５ ３０ １２６２ ５ ４０ １２８１ ５ ５０ １２９５ ６ ２０ １２４８ ６ ４０ １２９３ ６ ５０ １３０８ ７ ４０ １３０３ ７ ５０ １３１８[0009] Ti corresponding to each [% Ti] and [% N]
A typical example of the calculated value of the N solid solution temperature is as follows. Ti (ppm) N (ppm) TiN solid solution temperature (° C.) 330 1207 4 202 1224 4 30 1248 4 50 1281 4 60 1293 5 30 1262 5 40 1281 5 50 1295 6 20 1248 6 40 1293 6 50 1308 1303 7 50 1318
【００１０】本発明は、溶製した軸受鋼を鋳造する手段
として連続鋳造をとり、鋳造を、引き抜き速度０．４ｍ
／分以下の極低速連続鋳造により行なって鋳片とする。
このような極低速連続鋳造は、水冷モールドに注がれた
溶湯の凝固が速やかに進行することを図ったものであっ
て、偏析が改善され、粗大なＴｉ系介在物の生成が減少
することが期待される。According to the present invention, continuous casting is performed as a means for casting a smelted bearing steel, and the casting is performed at a drawing speed of 0.4 m.
/ Minute / min.
Such ultra-low-speed continuous casting aims at rapidly solidifying the molten metal poured into the water-cooled mold, and improves segregation and reduces generation of coarse Ti-based inclusions. There is expected.
【００１１】本発明に至る研究で、発明者らは、粗大な
Ｔｉ系介在物は連続鋳造における最終凝固部である濃化
溶鋼部に存在することを知り、その事実に対しては偏析
の影響が大きいと考えた。そして粗大Ｔｉ系介在物の生
成メカニズムを、つぎのように推測した。これに基づけ
ば、偏析の度合いは凝固速度に依存する。（デンドライ
ト樹間・先端におけるＴｉ・Ｎ・Ｃの偏析）→（Ｔｉ・
Ｎ・Ｃの溶解度積を超える温度までの温度低下）→（Ｔ
ｉＣ・ＴｉＮの晶出）→（晶出ＴｉＣ・ＴｉＮの成長）In the research leading to the present invention, the inventors have found that coarse Ti-based inclusions are present in the thickened molten steel portion, which is the final solidified portion in continuous casting, and the effect of segregation on this fact. Thought it was big. Then, the generation mechanism of the coarse Ti-based inclusions was estimated as follows. Based on this, the degree of segregation depends on the solidification rate. (Segregation of Ti ・ NC ・ C at dendrite tree / tip) → (Ti ・
Temperature drop to a temperature exceeding the solubility product of N / C) → (T
Crystallization of iC / TiN) → (Growth of crystallized TiC / TiN)
【００１２】図２は、引抜速度が０．４５ｍ／分の場合
と０．３０ｍ／分の場合とで、凝固の様子がどのように
異なるかを比較したものである。極低速連続鋳造であれ
ば、固液温度幅が小さくなり、凝固速度の向上と偏析の
改善が期待できる。FIG. 2 is a graph showing how the solidification differs between the case where the drawing speed is 0.45 m / min and the case where the drawing speed is 0.30 m / min. In the case of extremely low-speed continuous casting, the solid-liquid temperature width is reduced, and an improvement in the solidification rate and an improvement in segregation can be expected.
【００１３】極低速連続鋳造を行なうに当たり、固液温
度差の縮小、凝固速度の向上および偏析の低下をもたら
す操作は、すべて好ましい。具体的には、まずタンディ
ッシュヒーターの使用による低温鋳造があり、これはい
うまでもなく、固液温度差の縮小を意味する。電磁撹拌
も偏析の防止に有用であるが、とくに円形鋳型を使用し
て丸鋳片を鋳造する場合に適用すると、撹拌が効果的に
行なえる。適切な中心固相率における軽圧下は偏析の改
善につながり、二次冷却の強化は急速な凝固を引き起こ
す。これらの操作は、１種または２種以上、なるべく多
くを、上記の極低速連続鋳造に付加して実施することが
望ましい。[0013] In performing ultra-low speed continuous casting, all operations that reduce the solid-liquid temperature difference, improve the solidification rate, and reduce segregation are preferable. Specifically, first, there is a low-temperature casting using a tundish heater, which obviously means a reduction in the solid-liquid temperature difference. Electromagnetic stirring is also useful for preventing segregation, but when it is applied to the casting of round slabs using a circular mold, stirring can be performed effectively. Light reduction at an appropriate central solids fraction leads to improved segregation, and enhanced secondary cooling causes rapid solidification. It is desirable to carry out one or more of these operations, as much as possible, in addition to the above-mentioned extremely low speed continuous casting.
【００１４】本発明の方法において、分塊圧延により得
られたブルームを再度均熱温度に加熱する工程を付加す
れば、ＴｉＮを主体とするＴｉ系介在の微細化の目的
は、いっそうよく達成できる。分塊圧延により軸受鋼の
組織は細分化されており、その加工による微細化は容易
になるからである。[0014] In the method of the present invention, if the step of heating the bloom obtained by the slab rolling to the soaking temperature again is added, the object of miniaturization of Ti-based inclusions mainly composed of TiN can be further achieved. . This is because the structure of the bearing steel is subdivided by the slab rolling, and the refinement by the processing is facilitated.
【００１５】本発明の製造方法によりＴｉＮの粒子を微
細化することができる軸受鋼は、合金組成についていえ
ば、一般に、重量で、Ｃ：０．６〜１．５％，Ｓｉ：
２．０％以下，Ｍｎ：２．０％以下，Ｎｉ：０〜２．０
％，Ｃｒ：０．３〜５．０％およびＭｏ：０〜１．０％
を含有し、Ｔｉ：１０ppm以下、好ましくは７ppm以下、
Ｎ：５０ppm以下、好ましくは３０ppm以下であって、残
部が実質上Ｆｅからなるものである。[0015] The bearing steel which can make the particles of TiN fine by the production method of the present invention generally has a C: 0.6 to 1.5% by weight and a Si:
2.0% or less, Mn: 2.0% or less, Ni: 0 to 2.0
%, Cr: 0.3-5.0% and Mo: 0-1.0%
And Ti: 10 ppm or less, preferably 7 ppm or less,
N: 50 ppm or less, preferably 30 ppm or less, with the balance substantially consisting of Fe.
【００１６】[0016]
【実施例】下記の合金組成を有する軸受鋼（このＴｉＮ
固溶温度は、前記のように１２４０℃）を溶製し、引抜
速度０．４５ｍ／分または０．３０ｍ／分で連続鋳造
し、径３５０mmの丸鋳片を得た。 Ｃ Ｓｉ Ｍｎ Ｃｒ Ｍｏ Ｔｉ Ｎ Ｆｅ 1.0％ 0.25％ 0.45％ 1.5％ 0.1％ ３ppm 20ppm 残部EXAMPLE A bearing steel having the following alloy composition (this TiN
The solid solution temperature was 1240 ° C. as described above, and continuous casting was performed at a drawing speed of 0.45 m / min or 0.30 m / min to obtain a round slab having a diameter of 350 mm. CSiMnCrMoTiNFe 1.0% 0.25% 0.45% 1.5% 0.1% 3ppm 20ppm Remainder
【００１７】２種の丸鋳片について、１２６０℃×１０
時間の均熱処理を施したのち、横断方向および中心部に
おける軸方向のＴｉ系介在物を、３μｍ以上、５μｍ以
上および７．５μｍ以上の大きさ別に調べた。その結果
を、図３（比較例）および図４（実施例）に示す。For the two types of round slabs, 1260 ° C. × 10
After performing the soaking process for a long time, the Ti-based inclusions in the transverse direction and the axial direction in the central portion were examined by size of 3 μm or more, 5 μm or more, and 7.5 μm or more. The results are shown in FIG. 3 (Comparative Example) and FIG. 4 (Example).
【００１８】[0018]
【発明の効果】本発明の方法で軸受鋼を製造すれば、そ
の中のＴｉＮを中心とするＴｉ系介在物の粒子を微細化
することができる。この軸受鋼を材料にして、ＨＤＤ部
品などに需要の多い、音響特性のすぐれたミニチュアベ
アリング用ボールを製造することができる。When the bearing steel is manufactured by the method of the present invention, the particles of Ti-based inclusions centering on TiN therein can be refined. Using this bearing steel as a material, a ball for a miniature bearing having excellent acoustic characteristics, which is in great demand for HDD parts and the like, can be manufactured.
【図１】 軸受鋼の鋳片（Ｔｉ＝４ppm、Ｎ＝３０ppm）
を１１８０℃または１２４０℃に各６時間加熱したのち
の、Ｔｉ系介在物の粒度別の分布を、鋳造ままのものと
比較したグラフ。Fig. 1 Slab of bearing steel (Ti = 4ppm, N = 30ppm)
Is a graph comparing the distribution of Ti-based inclusions by particle size after being heated to 1180 ° C. or 1240 ° C. for 6 hours, respectively, as compared with the as-cast.
【図２】 本発明で採用する極低速連続鋳造を説明する
ための、水冷モールド付近の概念的な縦断面図で、引抜
速度が０．４５ｍ／分の場合と０．３０ｍ／分の場合と
を比較した図。FIG. 2 is a conceptual longitudinal sectional view showing a vicinity of a water-cooled mold for explaining an extremely low-speed continuous casting employed in the present invention, wherein a drawing speed is 0.45 m / min and a drawing speed is 0.30 m / min. FIG.
【図３】 本発明の比較例のデータであって、径３５０
mmの丸鋳片を引抜速度０．４５ｍ／分で連続鋳造した場
合の、横断方向および軸方向中心部のＴｉ系介在物の寸
法および個数を示すグラフ。FIG. 3 shows data of a comparative example of the present invention, wherein the diameter is 350;
The graph which shows the size and the number of Ti type | system | group inclusions of the transverse direction and the axial direction center part at the time of continuously casting a round cast piece of mm at a drawing speed of 0.45 m / min.
【図４】 本発明の実施例のデータであって、径３５０
mmの丸鋳片を引抜速度０．３０ｍ／分で連続鋳造した場
合の、横断方向および軸方向中心部のＴｉ系介在物の寸
法および個数を示すグラフ。FIG. 4 shows data of an embodiment of the present invention, wherein the diameter is 350;
The graph which shows the size and the number of Ti type | system | group inclusion of the center part of a transverse direction and an axial direction at the time of continuously casting the round cast piece of mm at a drawing speed of 0.30 m / min.
フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｂ２２Ｄ 11/12 Ｂ２２Ｄ 11/12 Ｃ 11/128 ３５０ 11/128 ３５０Ａ 11/20 11/20 Ａ 11/22 11/22 Ｂ // Ｃ２２Ｃ 38/00 ３０１ Ｃ２２Ｃ 38/00 ３０１Ｚ 38/58 38/58 Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat II (reference) B22D 11/12 B22D 11/12 C 11/128 350 11/128 350A 11/20 11/20 A 11/22 11/22 B // C22C 38/00 301 C22C 38/00 301Z 38/58 38/58
Claims (7)
超清浄軸受鋼を製造する方法であって、軸受鋼に必要な
合金成分を含有し、かつ、分塊圧延に先立つ均熱温度に
おいてＴｉＮが実質上固溶する限度内に［％Ｔｉ］×
［％Ｎ］の値を低減した合金組成をもつ軸受鋼を、連続
鋳造により鋳片に鋳造し、この鋳片または鋳塊を、均熱
温度としては固溶平衡温度以上の温度をえらび、均熱時
間としてはＴｉの拡散速度に基づいて決定される、Ｔｉ
Ｎの再固溶のためその粒子の径が減少するに足りる時間
をえらんだ均熱を施して、その後に分塊圧延および後続
の圧延を行なうことを特徴とする超清浄軸受鋼の製造方
法。1. A method for producing an ultra-clean bearing steel in which Ti carbonitrides are present in a fine state, comprising an alloy component necessary for the bearing steel, and a soaking temperature prior to slab rolling. [% Ti] × within the limit where TiN substantially dissolves
A bearing steel having an alloy composition with a reduced [% N] value is cast into a slab by continuous casting, and the slab or ingot is selected to have a temperature equal to or higher than a solid solution equilibrium temperature as a soaking temperature. The thermal time is determined based on the diffusion rate of Ti.
A method for producing an ultra-clean bearing steel, characterized in that a soaking is carried out for a time sufficient for reducing the diameter of the particles due to re-dissolution of N, followed by slab rolling and subsequent rolling.
軸受け鋼の鋳片を、１２００℃以上の温度に１時間以上
加熱する均熱処理を施し、長さが７．５μｍ以上のＴｉ
Ｎ粒子が実質上存在しない軸受鋼を得る請求項１の超清
浄軸受鋼の製造方法。2. A soaking slab of bearing steel having a titanium content of 10 ppm or less and a nitrogen content of 50 ppm or less is subjected to a soaking process of heating to a temperature of 1200 ° C. or more for 1 hour or more, and a Ti having a length of 7.5 μm or more.
2. The method for producing ultra-clean bearing steel according to claim 1, wherein a bearing steel substantially free of N particles is obtained.
以下の極低速連続鋳造により行なって鋳片とする請求項
１の超清浄軸受鋼の製造方法。3. The method for producing ultra-clean bearing steel according to claim 1, wherein the casting of the bearing steel is carried out by continuous casting at a very low speed at a drawing speed of 0.4 m / min or less to produce cast slabs.
ディッシュヒーターの使用による低温鋳造、円形鋳型の
使用とそれに対する電磁撹拌、適切な中心固相率におけ
る軽圧下、および二次冷却の強化の１種または２種以上
を付加して実施する請求項３の超清浄軸受鋼の製造方
法。4. In carrying out extremely low-speed continuous casting, one of low-temperature casting by using a tundish heater, use of a circular mold and electromagnetic stirring thereto, low pressure at an appropriate central solid phase ratio, and enhancement of secondary cooling. 4. The method for producing ultra-clean bearing steel according to claim 3, wherein the method is performed by adding one or more kinds.
再度均熱温度に加熱する工程を付加した請求項１ないし
４のいずれかの超清浄軸受鋼の製造方法。5. The method for producing an ultraclean bearing steel according to claim 1, further comprising a step of heating the bloom or billet after the bulk rolling to the soaking temperature again.
％，Ｓｉ：２．０％以下，Ｍｎ：２．０％以下，Ｎｉ：
０〜２．０％，Ｃｒ：０．３〜５．０％およびＭｏ：０
〜１．０％を含有し、Ｔｉ：１０ppm以下、Ｎ：５０ppm
以下であって、残部が実質上Ｆｅからなる合金組成を有
するものである請求項１ないし５のいずれかの超清浄軸
受鋼の製造方法。6. The bearing steel has a C: 0.6 to 1.5 by weight.
%, Si: 2.0% or less, Mn: 2.0% or less, Ni:
0 to 2.0%, Cr: 0.3 to 5.0%, and Mo: 0
-1.0%, Ti: 10 ppm or less, N: 50 ppm
The method for producing an ultra-clean bearing steel according to any one of claims 1 to 5, wherein the remainder has an alloy composition substantially consisting of Fe.
０ppm以下である請求項６の超清浄軸受鋼の製造方法。7. Ti: 7 ppm or less, N: 3 in bearing steel
The method for producing ultra-clean bearing steel according to claim 6, wherein the content is 0 ppm or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000250147A JP2002060887A (en) | 2000-08-21 | 2000-08-21 | Method for manufacturing high purity bearing steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000250147A JP2002060887A (en) | 2000-08-21 | 2000-08-21 | Method for manufacturing high purity bearing steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2002060887A true JP2002060887A (en) | 2002-02-28 |
Family
ID=18739774
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2000250147A Pending JP2002060887A (en) | 2000-08-21 | 2000-08-21 | Method for manufacturing high purity bearing steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2002060887A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010082662A (en) * | 2008-09-30 | 2010-04-15 | Kobe Steel Ltd | Forged product and crankshaft manufactured from the forged product |
| CN107208214A (en) * | 2015-01-23 | 2017-09-26 | 株式会社神户制钢所 | The bearing steel material and bearing parts of rolling contact fatigue excellent |
| CN109128063A (en) * | 2018-09-14 | 2019-01-04 | 武汉钢铁有限公司 | The method that TiN is mingled in the control slab of high-strength steel containing Ti |
-
2000
- 2000-08-21 JP JP2000250147A patent/JP2002060887A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010082662A (en) * | 2008-09-30 | 2010-04-15 | Kobe Steel Ltd | Forged product and crankshaft manufactured from the forged product |
| CN107208214A (en) * | 2015-01-23 | 2017-09-26 | 株式会社神户制钢所 | The bearing steel material and bearing parts of rolling contact fatigue excellent |
| CN109128063A (en) * | 2018-09-14 | 2019-01-04 | 武汉钢铁有限公司 | The method that TiN is mingled in the control slab of high-strength steel containing Ti |
| CN109128063B (en) * | 2018-09-14 | 2021-06-01 | 武汉钢铁有限公司 | Method for controlling TiN inclusions in Ti-containing high-strength steel casting blank |
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