JPH05140696A - Manufacture of bearing steel and bearing parts - Google Patents

Manufacture of bearing steel and bearing parts

Info

Publication number
JPH05140696A
JPH05140696A JP32637391A JP32637391A JPH05140696A JP H05140696 A JPH05140696 A JP H05140696A JP 32637391 A JP32637391 A JP 32637391A JP 32637391 A JP32637391 A JP 32637391A JP H05140696 A JPH05140696 A JP H05140696A
Authority
JP
Japan
Prior art keywords
bearing
steel
less
carburizing
shot peening
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
Application number
JP32637391A
Other languages
Japanese (ja)
Inventor
Takashi Ofuji
孝 大藤
Kunio Namiki
邦夫 並木
Original Assignee
Daido Steel Co Ltd
大同特殊鋼株式会社
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Daido Steel Co Ltd, 大同特殊鋼株式会社 filed Critical Daido Steel Co Ltd
Priority to JP32637391A priority Critical patent/JPH05140696A/en
Publication of JPH05140696A publication Critical patent/JPH05140696A/en
Granted legal-status Critical Current

Links

Abstract

PURPOSE:To provide the method for manufacturing bearing steel and bearing parts high in strength, having a prolonged service life and good in heat resistance. CONSTITUTION:The compsn. of bearing steel is constituted of, by weight, 0.15 to 0.25% C, 0.5 to 1.5% Si, 0.1 to 1.0% Mn, <=0.015% P, <=0.005% S, 0.5 to 3.5$ Ni, 0.5 to 2.5% Cr, 0.05 to 1.0% Mo, 0.05 to 1.0% V, <=0.003% Ti, 0.010 to 0.050% Al, 0.005 to 0.025% N, <=0.0010% O and balance substantial Fe and in which all grain diameter of oxide inclusions contained in the steel is regulated to <=15mum, and the ratio of the grains having >=10mum grain diameter is regulated to <2% in the whole. Furthermore, at the time of manufacturing bearing parts, the ant. of retained austenite after carburizing or carburizing and nitriding treatment to the above bearing steel is regulated to 15 to 35%; after that, it is subjected to hard shot peening treatment of >=0.7mmA arc height, and surface polishing is executed.

Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【産業上の利用分野】この発明は自動車等に用られる転
がり軸受部品等のための軸受鋼及び軸受部品の製造方法
に関する。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a bearing steel for rolling bearing parts used in automobiles and the like, and a method of manufacturing the bearing parts.

【0002】[0002]

【発明の背景】転がり軸受等の軸受部品は、自動車その
他の機械装置に広く用いられているが、近年自動車の軽
量化や高性能化等に伴って軸受部品も小型化し、また使
用条件も過酷となってきている。
BACKGROUND OF THE INVENTION Bearing parts such as rolling bearings are widely used in automobiles and other mechanical devices. In recent years, the bearing parts have been downsized with the weight reduction and high performance of automobiles, and the operating conditions are severe. Is becoming.

【0003】即ち軸受部品にかかる負荷が高負荷とな
り、作動速度も高速度化し、使用温度も高温化してきて
いる。
That is, the load applied to the bearing parts is high, the operating speed is increasing, and the operating temperature is increasing.

【0004】こうした中でかかる軸受部品の高強度化,
長寿命化,耐熱性の向上等が強く要望されている。
Under these circumstances, the strength of such bearing parts is increased,
There is a strong demand for longer life and improved heat resistance.

【0005】[0005]

【課題を解決するための手段】本発明はこのような事情
を背景としてなされたもので、その要旨は、軸受鋼組成
を、重量基準で、C:0.15%〜0.25%,Si:
0.5〜1.5%,Mn:0.1〜1.0%,P:0.
015%以下,S:0.005%以下,Ni:0.5〜
3.5%,Cr:0.5〜2.5%,Mo:0.05〜
1.0%,V:0.05〜1.0%,Ti:0.003
%以下,Al:0.010〜0.050%,N:0.0
05〜0.025%,O:0.0010%以下,残部実
質的にFeから成り、且つ鋼中に含まれる酸化物系介在
物が全て粒子径15μm以下であって、10μm以上の
粒子が全体の2%未満であるようになすことにある(請
求項1)。
SUMMARY OF THE INVENTION The present invention has been made in view of such circumstances, and the gist thereof is that the composition of a bearing steel is C: 0.15% to 0.25%, Si on a weight basis. :
0.5-1.5%, Mn: 0.1-1.0%, P: 0.
015% or less, S: 0.005% or less, Ni: 0.5 to
3.5%, Cr: 0.5 to 2.5%, Mo: 0.05 to
1.0%, V: 0.05 to 1.0%, Ti: 0.003
% Or less, Al: 0.010 to 0.050%, N: 0.0
05-0.025%, O: 0.0010% or less, the balance consisting essentially of Fe, and all oxide inclusions contained in the steel have a particle size of 15 μm or less, and particles of 10 μm or more as a whole. To be less than 2% (Claim 1).

【0006】また本願の別の発明は軸受部品の製造方法
に係るもので、請求項1の軸受鋼の浸炭又は浸炭・浸窒
処理後の残留オーステナイト量を15〜35%とし、そ
の後アークハイト0.7mmA以上のハードショットピ
ーニングを施して表面研磨することを特徴とする(請求
項2)。
Another aspect of the present invention relates to a method of manufacturing a bearing component, wherein the amount of retained austenite after carburizing or carburizing / nitriding treatment of the bearing steel of claim 1 is set to 15 to 35%, and then the arc height is set to 0. The surface is polished by performing hard shot peening of 0.7 mmA or more (claim 2).

【0007】従来、自動車の転がり軸受等の材料として
はSCr420等の材料が用いられているが、本発明で
はこれに対して焼戻し軟化抵抗の増大に有効なSi、焼
戻し軟化抵抗と焼入れ性向上,耐摩耗性向上に有効なC
rの含有量を高くするとともに、Crと同様焼戻し軟化
抵抗,焼入れ性,耐摩耗性増大に有効なMo、及び靱性
向上に有効なNiを含有させ、また結晶粒微細化元素と
してのV,Tiを所定量含有させるとともに、Oの含有
量を抑える等して組成,組織の適正化を図ったものであ
る。
Conventionally, materials such as SCr420 have been used as materials for rolling bearings of automobiles. In the present invention, however, Si which is effective in increasing temper softening resistance, temper softening resistance and improvement of hardenability, C effective for improving wear resistance
In addition to increasing the content of r, it also contains Mo, which is effective in increasing tempering softening resistance, hardenability and wear resistance, and Ni, which is effective in improving toughness, similar to Cr, and V and Ti as grain refinement elements. Is contained in a predetermined amount, and the content of O is suppressed to optimize the composition and structure.

【0008】また同時に鋼中の酸化物系介在物の量,大
きさを一定以下に抑えたものであり、このような素材の
改善によって軸受部品の高強度化,長寿命化,耐熱化を
達成した。
[0008] At the same time, the amount and size of oxide inclusions in the steel are kept below a certain level. By improving such materials, bearing parts can have higher strength, longer life, and higher heat resistance. did.

【0009】本発明において上記各種成分の添加理由及
び限定理由を更に詳述すると以下の如くである。 C:0.15〜0.25% Cは心部硬さ,焼入れ・焼戻し硬さを得るために0.1
5%以上必要である。しかしながら0.25%を超えて
含有させると巨大炭化物が生成し、心部の靱性が低下す
る。
The reasons for adding and limiting the above-mentioned various components in the present invention will be described in more detail below. C: 0.15 to 0.25% C is 0.1 to obtain core hardness, quenching / tempering hardness.
5% or more is required. However, if the content exceeds 0.25%, huge carbides are formed, and the toughness of the core is reduced.

【0010】Si:0.5〜1.5% Siは焼戻し軟化抵抗の増大に有効な成分であって、そ
のためには0.5%以上が必要である。但しSiは浸炭
性を阻害し、またSi添加により変態点が上昇し、十分
に焼きを入れるにはより高温に加温しなければならず、
これは結晶粒の粗大化を招く。従ってこの発明では上限
値を1.5%とする。
Si: 0.5 to 1.5% Si is an effective component for increasing temper softening resistance, and 0.5% or more is necessary for that. However, Si impairs carburizing properties, and the transformation point rises due to the addition of Si, so it is necessary to heat it to a higher temperature in order to sufficiently quench it.
This leads to coarsening of crystal grains. Therefore, in the present invention, the upper limit value is set to 1.5%.

【0011】Mn:0.1〜1.0% Mnは焼入れ性確保のために0.1%以上必要である。
しかしながら1.0%を超えると靱性が劣化し、また非
金属介在物の量が増加してしまう。
Mn: 0.1 to 1.0% Mn is required to be 0.1% or more to secure hardenability.
However, if it exceeds 1.0%, the toughness deteriorates and the amount of nonmetallic inclusions increases.

【0012】Ni:0.5〜3.5% Niは靱性向上効果が大きく、亀裂進展を阻害する効果
が高い。但し0.5%より少ないとその効果は期待でき
ず、また3.5%よりも多いと残留オ−ステナイト量が
増加し、十分な焼入れ硬さが得られなくなる。
Ni: 0.5 to 3.5% Ni has a large effect of improving the toughness and a high effect of inhibiting crack growth. However, if it is less than 0.5%, its effect cannot be expected, and if it is more than 3.5%, the amount of retained austenite increases, and sufficient quenching hardness cannot be obtained.

【0013】Cr:0.5〜2.5% Crは0.5%以上添加することによってSi添加によ
る焼入れ性の減少分を補って焼入れ性を確保し、また焼
戻し軟化抵抗の付与に効果がある。またその炭化物は耐
摩耗性を向上させる。
Cr: 0.5 to 2.5% By adding 0.5% or more of Cr, the hardenability is ensured by compensating for the decrease in the hardenability due to the addition of Si, and it is effective in imparting temper softening resistance. is there. Further, the carbide improves wear resistance.

【0014】しかしながらCrは巨大炭化物を生成し易
く、通常のガス浸炭では浸炭層に粒界酸化された層を形
成するため、2.5%より多く添加するのは望ましくな
い。
However, since Cr easily forms a huge carbide, and a normal gas carburizing forms a grain boundary oxidized layer in the carburized layer, it is not desirable to add more than 2.5%.

【0015】Mo:0.05〜1.0% MoはCrと同様、炭化物生成元素であり、0.05%
以上添加することによって焼入れ性,焼戻し軟化抵抗
性,耐摩耗性向上に効果がある。
Mo: 0.05 to 1.0% Mo is a carbide-forming element, similar to Cr, and is 0.05%.
The above additions have the effect of improving hardenability, temper softening resistance, and wear resistance.

【0016】但し1.0%より多量に添加しても効果は
飽和し、また巨大炭化物を生成する恐れがある。またこ
のMoは高価な元素であり、コスト面からも1.0%以
下に抑えるのが良い。
However, even if added in an amount of more than 1.0%, the effect is saturated and there is a possibility that huge carbides will be formed. Further, this Mo is an expensive element, and it is preferable to suppress it to 1.0% or less in terms of cost.

【0017】V:0.05〜1.0% Vは結晶粒の微細化に有効であり、0.05%以上の少
量添加で大きな効果が得られる。但し1.0%を超えて
添加しても効果は飽和し、またコスト的にも不利とな
る。
V: 0.05 to 1.0% V is effective for refining crystal grains, and a large effect can be obtained by adding a small amount of 0.05% or more. However, even if added in excess of 1.0%, the effect is saturated, and there is a cost disadvantage.

【0018】Ti:0.003%以下 Tiは少量添加するだけで結晶粒微細化に効果がある。
但し一定量以上に添加するとTiN粗大化による寿命低
下を来す。従ってTiは0.003%以下とする必要が
ある。
Ti: 0.003% or less Only a small amount of Ti is effective in refining crystal grains.
However, if it is added in a certain amount or more, the life is shortened due to coarsening of TiN. Therefore, Ti needs to be 0.003% or less.

【0019】Al:0.010〜0.050% AlはAlNを生成して結晶粒を微細化する効果があ
る。但しこの効果を得るためには0.010%以上が必
要である。
Al: 0.010 to 0.050% Al has the effect of producing AlN and refining the crystal grains. However, to obtain this effect, 0.010% or more is necessary.

【0020】一方0.050%よりも多く添加しても効
果が飽和するばかりでなく、却って粗大な析出物を生成
して寿命を低下させる原因となる。
On the other hand, addition of more than 0.050% not only saturates the effect, but rather causes formation of coarse precipitates and shortens the life.

【0021】P:0.015%以下 Pは靱性を劣化させる原因となる元素であり、0.01
5%以下に抑える必要がある。
P: 0.015% or less P is an element causing deterioration of toughness, and 0.01
It is necessary to keep it below 5%.

【0022】S:0.005%以下 Sは粗大なMnSを形成して寿命を低下させる。本発明
では0.005%以下に抑える。
S: 0.005% or less S forms coarse MnS and shortens the life. In the present invention, it is suppressed to 0.005% or less.

【0023】N:0.005〜0.025% NはAl,V,Ti等と結合し、結晶粒を微細化させ
る。但しこの効果を得るためには0.005%以上が必
要で、逆に0.025%よりも多くなると靱性を劣化さ
せてしまう。
N: 0.005 to 0.025% N bonds with Al, V, Ti, etc. to make crystal grains finer. However, in order to obtain this effect, 0.005% or more is necessary, and conversely, if it exceeds 0.025%, the toughness is deteriorated.

【0024】O:0.0010%以下 Oは種々の元素と酸化物を形成し、寿命を低下させる。
この発明ではこれをできるだけ防止すべく0.0010
%以下とする。
O: 0.0010% or less O forms an oxide with various elements and shortens the life.
In the present invention, in order to prevent this as much as possible, 0.0010
% Or less.

【0025】請求項2の発明は、請求項1の軸受鋼より
軸受部品を製造するに際しての処理方法に特徴を有する
もので、この方法では浸炭処理後の残留オ−ステナイト
を所定量となし、その後ハードショットピーニング,表
面研磨を行うものである。
A second aspect of the present invention is characterized by a treatment method for producing a bearing component from the bearing steel according to the first aspect. In this method, residual austenite after carburizing treatment is set to a predetermined amount, After that, hard shot peening and surface polishing are performed.

【0026】転がり軸受等の軸受部品は表面の精度が要
求されることから、一般にはこのようなショットピーニ
ングを施さないで使用する。
Since bearing parts such as rolling bearings are required to have high surface accuracy, they are generally used without such shot peening.

【0027】本発明においてかかるショットピーニング
を施しているのは、このショットピーニング自身の効果
によって表面に残留圧縮応力を生ぜしめるとともに、残
留オ−ステナイトから加工誘起マルテンサイトを生成せ
しめ、このマルテンサイト層による表面硬化作用と、マ
ルテンサイト層生成に伴う膨張によって表層の残留圧縮
応力を更に高めることで、軸受部品の疲労強度を高める
ためである。
In the present invention, the shot peening is performed because the effect of the shot peening itself causes a residual compressive stress on the surface, and at the same time, a process-induced martensite is generated from the retained austenite, and this martensite layer is formed. This is to increase the fatigue strength of the bearing component by further increasing the residual compressive stress of the surface layer by the surface hardening action by the above and the expansion accompanying the formation of the martensite layer.

【0028】但しこのようなショットピーニングを施す
と軸受部品の表面が荒れてしまうため、その後に研磨を
施して表面を平滑化するようにしており、そしてそのよ
うな研磨を施したときに表層の残留圧縮応力の生じた部
分が全て除去されてしまわないように、アークハイト
0.7mmA以上のハードショットピーニングを施すよ
うにしている。
However, since the surface of the bearing component becomes rough when such shot peening is applied, the surface is smoothed by polishing after that, and the surface layer of the surface layer when such polishing is applied. Hard shot peening with an arc height of 0.7 mmA or more is performed so that the portion where the residual compressive stress is generated is not completely removed.

【0029】このようなハードショットピーニングと表
面研磨とを組み合わせることで、表層の圧縮応力の残留
と表面の平滑化とをともに達成し、疲労寿命の向上を図
ることができた。
By combining such hard shot peening and surface polishing, residual compressive stress in the surface layer and smoothing of the surface were both achieved, and the fatigue life could be improved.

【0030】[0030]

【実施例】次に本発明の特徴を更に明確にすべく、以下
にその実施例を詳述する。表1に示す組成の鋼を用いて
次の手順及び条件に従い各種試験を行った。
EXAMPLES In order to further clarify the characteristics of the present invention, examples thereof will be described in detail below. Various tests were conducted using steels having the compositions shown in Table 1 according to the following procedures and conditions.

【0031】即ち表1に示す組成から成る供試材の酸化
物系介在物の測定を行うとともに、供試材を加工して試
験片を得、これを図1に示す条件で浸炭焼入れ・焼戻し
処理を行って残留オーステナイト量を測定した。
That is, while measuring oxide inclusions of the test material having the composition shown in Table 1, the test material was processed to obtain a test piece, which was carburized and tempered under the conditions shown in FIG. The treatment was performed to measure the amount of retained austenite.

【0032】その後、処理材に対してアークハイト0.
7mmAのハードショットピーニング,アークハイト
0.2mmAの弱いショットピーニングをそれぞれ施し
たもの及び比較としてこのようなショットピーニングを
施さないものについて表面研磨加工し、表層0.05m
mを除去し、表面硬さ,残留応力測定を行った。
After that, the arc height of 0.
Hard shot peening of 7 mmA, weak shot peening of arc height 0.2 mmA, and those without such shot peening for comparison were surface-polished to give a surface layer of 0.05 m.
After removing m, surface hardness and residual stress were measured.

【0033】尚この測定は、比較のため表面研磨を行わ
なかったものについても行った。
For comparison, this measurement was also carried out on the surface-polished ones.

【0034】次に以上の工程を経た試料を転動寿命試験
に供し、負荷回数46240cpm,負荷応力5884
N/mm2の条件でラジアル型転動寿命試験を行った。
これらの結果が表2に示してある。
Next, the sample that has undergone the above steps is subjected to a rolling life test, and the load frequency is 46240 cpm and the load stress is 5884.
A radial rolling life test was conducted under the condition of N / mm 2 .
The results are shown in Table 2.

【0035】[0035]

【表1】 [Table 1]

【0036】[0036]

【表2】 [Table 2]

【0037】表2において明らかなように、酸化物系介
在物の量,大きさ共に十分に低い鋼種A,B,C,Dに
ついても、アークハイト0.2mmA程度の弱いショッ
トピーニングでは、その後の表面研磨によって圧縮残留
応力が失われてしまい、疲労寿命がそれ程延びないこ
と、寿命を延ばすにはアークハイト0.7mmA以上の
ハードショットピーニングが必要であることが分かっ
た。
As is clear from Table 2, even for steel types A, B, C and D in which the amount and size of the oxide-based inclusions are sufficiently low, after the weak shot peening with an arc height of about 0.2 mmA, It was found that the compressive residual stress was lost by the surface polishing, the fatigue life was not extended so much, and hard shot peening with an arc height of 0.7 mmA or more was required to extend the life.

【0038】また表2の結果においては、鋼種A,B,
C,Dの順に寿命値が延びているが、これは酸化物系介
在物の量,大きさの低下による効果、V,Tiによる結
晶粒微細化の効果及びSi,Ni量の増加による焼戻し
軟化抵抗の増加による効果の表れであると考えられる。
Further, in the results of Table 2, steel types A, B,
The life value increases in the order of C and D. This is due to the effect of decreasing the amount and size of oxide inclusions, the effect of refining crystal grains due to V and Ti, and the temper softening due to the increase of Si and Ni contents. This is considered to be a manifestation of the effect due to the increase in resistance.

【0039】尚No.4と15との比較から、疲労寿命
に対する酸化物系介在物の量と大きさとの直接的な影響
を確認することができる。
No. From the comparison between 4 and 15, it is possible to confirm the direct influence of the amount and size of the oxide-based inclusions on the fatigue life.

【0040】以上本発明の実施例を詳述したがこれはあ
くまで一例示であり、本発明はその主旨を逸脱しない範
囲において、様々な変更を加えた態様で実施可能であ
る。
Although the embodiment of the present invention has been described in detail above, this is merely an example, and the present invention can be implemented in various modified modes without departing from the spirit of the invention.

【図面の簡単な説明】[Brief description of drawings]

【図1】本発明の実施例において採用した浸炭焼入れ・
焼戻しの条件を示す図である。
FIG. 1 Carburizing and quenching adopted in the embodiment of the present invention
It is a figure which shows the conditions of tempering.

───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.5 識別記号 庁内整理番号 FI 技術表示箇所 C23C 8/22 8116−4K 8/26 8116−4K ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 5 Identification code Internal reference number FI technical display location C23C 8/22 8116-4K 8/26 8116-4K

Claims (2)

【特許請求の範囲】[Claims] 【請求項1】 重量基準で C :0.15〜0.25% Si:0.5〜1.
5% Mn:0.1〜1.0% P :0.015%
以下 S :0.005%以下 Ni:0.5〜3.
5% Cr:0.5〜2.5% Mo:0.05〜
1.0% V :0.05〜1.0% Ti:0.003%
以下 Al:0.010〜0.050% N :0.005〜
0.025% O:0.0010%以下 残部実質的にFeから成り、且つ鋼中に含まれる酸化物
系介在物が全て粒子径15μm以下であって、10μm
以上の粒子が全体の2%未満であることを特徴とする軸
受鋼。
1. C: 0.15-0.25% Si: 0.5-1.
5% Mn: 0.1-1.0% P: 0.015%
Hereinafter S: 0.005% or less Ni: 0.5 to 3.
5% Cr: 0.5-2.5% Mo: 0.05-
1.0% V: 0.05-1.0% Ti: 0.003%
Below Al: 0.010 to 0.050% N: 0.005
0.025% O: 0.0010% or less The balance consists essentially of Fe, and all oxide inclusions contained in the steel have a particle size of 15 μm or less and 10 μm.
Bearing steel characterized in that the above particles are less than 2% of the whole.
【請求項2】 請求項1の軸受鋼の浸炭又は浸炭・浸窒
処理後の残留オーステナイト量を15〜35%とし、そ
の後アークハイト0.7mmA以上のハードショットピ
ーニングを施して表面研磨することを特徴とする軸受部
品の製造方法。
2. The amount of retained austenite after carburizing or carburizing / nitriding treatment of the bearing steel according to claim 1 is set to 15 to 35%, and then hard shot peening with an arc height of 0.7 mmA or more is applied to surface polish. A method for manufacturing a characteristic bearing component.
JP32637391A 1991-11-14 1991-11-14 Manufacture of bearing steel and bearing parts Granted JPH05140696A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP32637391A JPH05140696A (en) 1991-11-14 1991-11-14 Manufacture of bearing steel and bearing parts

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP32637391A JPH05140696A (en) 1991-11-14 1991-11-14 Manufacture of bearing steel and bearing parts

Publications (1)

Publication Number Publication Date
JPH05140696A true JPH05140696A (en) 1993-06-08

Family

ID=18187079

Family Applications (1)

Application Number Title Priority Date Filing Date
JP32637391A Granted JPH05140696A (en) 1991-11-14 1991-11-14 Manufacture of bearing steel and bearing parts

Country Status (1)

Country Link
JP (1) JPH05140696A (en)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1996022404A1 (en) * 1995-01-18 1996-07-25 Nippon Steel Corporation Long-lived carburized bearing steel
CN1059715C (en) * 1998-10-08 2000-12-20 冶金工业部钢铁研究总院 High strength and high toughness secondary hardened steel
EP1138795A1 (en) * 1999-08-27 2001-10-04 Koyo Seiko Co., Ltd. Law material for bearing parts
KR20030070316A (en) * 2002-02-23 2003-08-30 주식회사 제철기전 Method for producing of high function bearing steel
DE19960235B4 (en) * 1998-12-25 2004-05-27 Jfe Steel Corp. Rolling
EP1512761A1 (en) * 2003-08-28 2005-03-09 Nissan Motor Company, Limited Contact pressure-resistant member and method of making the same
KR100736144B1 (en) * 2006-01-09 2007-07-06 송기성 A touch jig for a automatic measuring machine
WO2019142947A1 (en) 2018-01-22 2019-07-25 日本製鉄株式会社 Carburized bearing steel component, and steel bar for carburized bearing steel component

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1996022404A1 (en) * 1995-01-18 1996-07-25 Nippon Steel Corporation Long-lived carburized bearing steel
US5698159A (en) * 1995-01-18 1997-12-16 Nippon Steel Corporation Long-life carburizing bearing steel
CN1059715C (en) * 1998-10-08 2000-12-20 冶金工业部钢铁研究总院 High strength and high toughness secondary hardened steel
DE19960235B4 (en) * 1998-12-25 2004-05-27 Jfe Steel Corp. Rolling
DE19960235B8 (en) * 1998-12-25 2005-06-09 Jfe Steel Corp. roller bearing
EP1138795A1 (en) * 1999-08-27 2001-10-04 Koyo Seiko Co., Ltd. Law material for bearing parts
EP1138795A4 (en) * 1999-08-27 2004-11-10 Koyo Seiko Co Law material for bearing parts
KR20030070316A (en) * 2002-02-23 2003-08-30 주식회사 제철기전 Method for producing of high function bearing steel
EP1512761A1 (en) * 2003-08-28 2005-03-09 Nissan Motor Company, Limited Contact pressure-resistant member and method of making the same
KR100736144B1 (en) * 2006-01-09 2007-07-06 송기성 A touch jig for a automatic measuring machine
WO2019142947A1 (en) 2018-01-22 2019-07-25 日本製鉄株式会社 Carburized bearing steel component, and steel bar for carburized bearing steel component
KR20200102488A (en) 2018-01-22 2020-08-31 닛폰세이테츠 가부시키가이샤 Carburized bearing steel parts and rods for carburized bearing steel parts

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