JP2724019B2 - Heat-resistant bearing steel - Google Patents
Heat-resistant bearing steelInfo
- Publication number
- JP2724019B2 JP2724019B2 JP2047302A JP4730290A JP2724019B2 JP 2724019 B2 JP2724019 B2 JP 2724019B2 JP 2047302 A JP2047302 A JP 2047302A JP 4730290 A JP4730290 A JP 4730290A JP 2724019 B2 JP2724019 B2 JP 2724019B2
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- temperature
- fatigue life
- steel
- hardness
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Description
【発明の詳細な説明】 （産業上の利用分野） この発明は、ころ軸受、玉軸受といった転がり軸受の
要素部材に加工するための軸受鋼の改良に関し、この種
の軸受の使用環境の過酷化、なかでも高速化、高面圧化
に伴う使用温度の上昇に対応して、150℃から250℃に至
るような高温（以下単に「高温」という）で使用して
も、すぐれた転動疲労寿命特性を発揮することができ
る、使用許容温度の高い耐熱軸受用鋼を提案しようとす
るものである。Description: BACKGROUND OF THE INVENTION The present invention relates to an improvement in bearing steel for processing into an element member of a rolling bearing such as a roller bearing and a ball bearing, and the use environment of this type of bearing is severe. Excellent rolling fatigue even when used at high temperatures ranging from 150 ° C to 250 ° C (hereinafter simply referred to as “high temperature”) in response to the increase in operating temperature accompanying higher speed and higher surface pressure. An object of the present invention is to propose a heat-resistant bearing steel having a high allowable use temperature and capable of exhibiting life characteristics.
転がり軸受は、その負荷回転に基く温度上昇の下での
寸法安定性、転動疲労寿命を保証するために、熱処理時
の焼戻温度と焼戻後の表面硬度により使用許容温度が設
定される。たとえば、軸受用鋼として広く利用されて来
た、JIS高炭素クロム軸受鋼SUJ2は、転がり軸受として
必要な硬度に調整するため、通常180℃の焼戻処理が施
され、転がり軸受の負荷時における転動表面での過度な
温度上昇を避けるように、使用温度範囲は一般に120℃
以下とされる。In order to guarantee the dimensional stability and the rolling fatigue life of the rolling bearing under temperature rise due to the load rotation, the allowable operating temperature is set by the tempering temperature during heat treatment and the surface hardness after tempering. . For example, JIS high carbon chromium bearing steel SUJ2, which has been widely used as bearing steel, is usually tempered at 180 ° C in order to adjust to the required hardness as a rolling bearing. Operating temperature range is generally 120 ° C to avoid excessive temperature rise on the rolling surface
It is as follows.
（従来の技術） 特公昭54-41014号公報には、常温ならびに高温におけ
る特性の優れた転がり軸受用鋼に関する開示があり、ま
た、特開昭63-62847号公報には、ガスタービンなど熱機
関の回転主軸の軸受のように高速下で300℃以上のよう
な高い温度で使用するための耐熱軸受用鋼が開示されて
いるが、これらはいずれも炭化物形成元素を多量に添加
する必要がある。(Prior Art) Japanese Patent Publication No. 54-41014 discloses a rolling bearing steel having excellent characteristics at normal temperature and high temperature, and Japanese Patent Application Laid-Open No. 63-62847 discloses a heat engine such as a gas turbine. Heat-resistant bearing steels for use at high temperatures, such as 300 ° C or higher, at high speeds such as rotating spindle bearings have been disclosed, but all of these require the addition of a large amount of carbide-forming elements. .
これらのほかさらに、高温焼戻による二次析出硬化を
図った高速度工具鋼を転がり軸受に用いることも知られ
ている。In addition to these, it is also known to use a high-speed tool steel for secondary precipitation hardening by high-temperature tempering for a rolling bearing.
しかし、多量の合金元素を添加するとき、偏析をなく
すために長時間の均熱保持が加工上必要なこと、また熱
処理のためにも高温長時間にわたる加熱が必要になるこ
と、さらに合金成分添加コストが嵩むことなど、生産性
ないしはコストの面で不利が著しいといった問題点があ
る。However, when adding a large amount of alloying elements, it is necessary to maintain a long-term soaking in order to eliminate segregation, and it is necessary to heat for a long time at high temperature for heat treatment. There is a problem that productivity or cost is disadvantageous, such as an increase in cost.
（発明が解決しようとする課題） 転がり軸受の使用条件の過酷化、なかでも高速化、高
面圧化に伴う、軸受用鋼の使用許容温度の150℃ないし2
50℃に及ぶような高温化の要求については、JIS高炭素
クロム軸受鋼鋼材SUJ2にくらべて、 １）高温焼戻による硬度低下が少ないこと、 ２）高温度域で、優れた転動疲労寿命特性を有するこ
と、 を必要とする。(Problems to be Solved by the Invention) Due to the severe operating conditions of rolling bearings, especially high speed and high surface pressure, the allowable operating temperature of bearing steel is 150 ° C to 2 ° C.
As for the requirement of high temperature up to 50 ° C, compared to JIS high carbon chromium bearing steel SUJ2, 1) less decrease in hardness due to high temperature tempering, 2) excellent rolling fatigue life in high temperature range It must have characteristics.
そこでこの発明は、上記した従来の技術の問題点に鑑
み、製造コストの増加を極力抑制してしかも高温での転
動疲労寿命特性に優れた耐熱軸受用鋼を安価に提供する
ことを目的とするものである。Accordingly, an object of the present invention is to provide a low-cost steel for heat-resistant bearings, which suppresses an increase in manufacturing cost as much as possible and has excellent rolling fatigue life characteristics at high temperatures, in view of the above-mentioned problems of the conventional technology. Is what you do.
（課題を解決するための手段） この発明は、発明者らが軸受用鋼の使用許容温度を向
上させる目的で、焼戻後の硬度ならびに高温条件下での
転動疲労寿命におよぼす炭化物の影響について研究を重
ねた結果、合金元素を多量に添加しなくとも、Cr量の微
増と、とくにSiとMoとの適量含有による相乗作用によ
り、高温度での焼戻においても必要とする硬度が得られ
て高温の使用条件下で優れた転がり軸受の転動疲労寿命
特性が得られることを見出したもので、その要旨は以下
のとおりである。(Means for Solving the Problems) In order to improve the allowable working temperature of bearing steel, the present invention provides an effect of carbides on hardness after tempering and rolling fatigue life under high temperature conditions. As a result of repeated studies, the hardness required for tempering at high temperatures can be obtained even without adding a large amount of alloying elements, due to the slight increase in the amount of Cr and the synergistic effect due to the appropriate content of Si and Mo. It has been found that excellent rolling contact fatigue life characteristics of rolling bearings can be obtained under high temperature use conditions, and the gist thereof is as follows.
1.C:0.8wt％以上、1.5wt％以下、 Si:0.5wt％以上、2.0wt％以下、 Mn:0.3wt％以上、2.0wt％以下、 Cr:1.3wt％以上、1.98wt％以下、及び Mo:0.3wt％以上、1.0wt％以下 を、 SiとMoの合計で1.0wt％以上、 を満足する範囲で含有し、残部は鉄及び不可避不純物の
組成になる耐熱軸受用鋼。1.C: 0.8wt% or more, 1.5wt% or less, Si: 0.5wt% or more, 2.0wt% or less, Mn: 0.3wt% or more, 2.0wt% or less, Cr: 1.3wt% or more, 1.98wt% or less, And Mo: 0.3 wt% or more and 1.0 wt% or less, in a range satisfying 1.0 wt% or more in total of Si and Mo, with the balance being iron and unavoidable impurities.
2.C:0.8wt％以上、1.5wt％以下、 Si:0.5wt％以上、2.0wt％以下、 Mn:0.3wt％以上、2.0wt％以下、 Cr:1.3wt％以上、1.98wt％以下、及び Mo:0.3wt％以上、1.0wt％以下 を、 SiとMoの合計で1.0wt％以上、 を満足する範囲で含有し、かつ、 W:0.05wt％以上、0.50wt％以下、及び V:0.05wt％以上、0.50wt％以下、 のうちから選んだ１種又は２種を含有し、残部は鉄及び
不可避不純物の組成になる耐熱軸受用鋼。2.C: 0.8wt% or more, 1.5wt% or less, Si: 0.5wt% or more, 2.0wt% or less, Mn: 0.3wt% or more, 2.0wt% or less, Cr: 1.3wt% or more, 1.98wt% or less, And Mo: 0.3 wt% or more and 1.0 wt% or less, in a range satisfying the following: 1.0 wt% or more in total of Si and Mo, and W: 0.05 wt% or more and 0.50 wt% or less, and V: Heat-resistant bearing steel containing one or two selected from 0.05wt% or more and 0.50wt% or less, with the balance being iron and unavoidable impurities.
3.C:0.8wt％以上、1.5wt％以下、 Si:0.5wt％以上、2.0wt％以下、 Mn:0.3wt％以上、2.0wt％以下、 Cr:1.3wt％以上、1.98wt％以下、及び Mo:0.3wt％以上、1.0wt％以下 を、 SiとMoの合計で1.0wt％以上、 を満足する範囲で含有し、かつ、 Ni:0.1wt％以上、2.0wt％以下，及び Cu:0.05wt％以上、1.00wt％以下、 のうちから選んだ１種又は２種を含有し、残部は鉄及び
不可避不純物の組成になる耐熱軸受用鋼。3.C: 0.8wt% or more, 1.5wt% or less, Si: 0.5wt% or more, 2.0wt% or less, Mn: 0.3wt% or more, 2.0wt% or less, Cr: 1.3wt% or more, 1.98wt% or less, And Mo: 0.3 wt% or more and 1.0 wt% or less, in a range satisfying the following: 1.0 wt% or more in total of Si and Mo, and Ni: 0.1 wt% or more and 2.0 wt% or less, and Cu: Heat-resistant bearing steel containing one or two selected from the group consisting of 0.05 wt% or more and 1.00 wt% or less, with the balance being iron and unavoidable impurities.
4.C:0.8wt％以上、1.5wt％以下、 Si:0.5wt％以上、2.0wt％以下、 Mn:0.3wt％以上、2.0wt％以下、 Cr:1.3wt％以上、1.98wt％以下、及び Mo:0.3wt％以上、1.0wt％以下 を、 SiとMoの合計で1.0wt％以上、 を満足する範囲で含有し、かつ、 W:0.05wt％以上、0.50wt％以下、及び V:0.05wt％以上、0.50wt％以下、 のうちから選んだ１種又は２種以上と、 Ni:0.1wt％以上、2.0wt％以下， Cu:0.05wt％以上、1.0wt％以下、 のうちから選んだ１種又は２種以上を含有し、残部は鉄
及び不可避不純物の組成になる耐熱軸受用鋼。4.C: 0.8wt% or more, 1.5wt% or less, Si: 0.5wt% or more, 2.0wt% or less, Mn: 0.3wt% or more, 2.0wt% or less, Cr: 1.3wt% or more, 1.98wt% or less, And Mo: 0.3 wt% or more and 1.0 wt% or less, in a range satisfying the following: 1.0 wt% or more in total of Si and Mo, and W: 0.05 wt% or more and 0.50 wt% or less, and V: One or more selected from 0.05 wt% or more and 0.50 wt% or less, and Ni: 0.1 wt% or more and 2.0 wt% or less, Cu: 0.05 wt% or more and 1.0 wt% or less Heat-resistant bearing steel containing one or more selected components, with the balance being iron and unavoidable impurities.
なお、この発明では、鋼中酸素量の低減および介在物
の形態制御のため、Ca:0.05wt％以下、Na:0.05wt％以
下、K:0.05wt％以下、Mg:0.1wt％以下、及びZr:0.1wt％
以下のうちから選んだ少なくとも一種を含有すること、
また、被削性の向上には、B:0.05wt％以下、S:0.25wt％
以下、Ca:0.01wt％以下、Pb:0.3wt％以下、Bi:0.3wt％
以下、及びREM:0.25wt％以下のうちから選んだ少なくと
も一種を含有すること、熱間強度の向上を目指して、P:
0.1wt％以下、及びN:0.05wt％以下のうちから選んだ少
なくとも一種を含有すること、さらには、脱炭防止のた
めにSb:0.05wt％以下を含有することのような各場合に
も、所期の目的に対し格別の不利を伴うことなくして、
それぞれの所期するところが実現され得る。In the present invention, in order to reduce the oxygen content in steel and control the form of inclusions, Ca: 0.05 wt% or less, Na: 0.05 wt% or less, K: 0.05 wt% or less, Mg: 0.1 wt% or less, and Zr: 0.1wt%
Contain at least one selected from the following,
To improve machinability, B: 0.05 wt% or less, S: 0.25 wt%
Below, Ca: 0.01 wt% or less, Pb: 0.3 wt% or less, Bi: 0.3 wt%
With the aim of containing at least one selected from the following, and REM: 0.25 wt% or less, and improving hot strength, P:
0.1 wt% or less, and N: at least one selected from 0.05 wt% or less, and even in each case such as containing Sb: 0.05 wt% or less to prevent decarburization. , Without any particular disadvantage to the intended purpose,
Each desired point can be realized.
（作用） この発明による耐熱軸受用鋼において、その合金成分
の組織範囲を限定する理由について次に述べる。(Operation) The reason for limiting the range of the structure of the alloy component in the heat-resistant bearing steel according to the present invention will be described below.
C:基地に固溶しマルテンサイトを強化し、焼戻後の硬度
確保と転動疲労寿命特性の向上にも役立つためには0.8w
t％を必要とする。しかし多すぎると巨大炭化物が生成
した転動疲労寿命特性を劣化させるので1.5wt％を上限
とする。C: 0.8w to form a solid solution in the matrix to strengthen martensite, to secure hardness after tempering and to improve rolling fatigue life characteristics
Requires t%. However, if the content is too large, the rolling fatigue life characteristics of the generated carbides deteriorate, so the upper limit is 1.5 wt%.
Si:鋼の溶製時に脱酸剤として作用するほか、基地に固
溶して後述のMoとの相互作用の下で、とくに焼戻後の硬
度低下の抑制に寄与するように0.5wt％を必要とする。
しかし、多すぎると被削性ならびに鍛造性を著しく劣化
させるので、上限を2.0wt％とするが、1.0wt％未満がよ
り好ましい。Si: In addition to acting as a deoxidizing agent when smelting steel, it also forms a solid solution in the matrix and, under the interaction with Mo described below, contributes 0.5 wt% to contribute to the suppression of the decrease in hardness, especially after tempering. I need.
However, if the content is too large, the machinability and forgeability are remarkably deteriorated. Therefore, the upper limit is set to 2.0% by weight, but less than 1.0% by weight is more preferable.
Mn:鋼の焼入性を向上させることにより基地マルテンサ
イトの靭性を高め、鋼材の硬度ならびに転動疲労寿命を
向上させるため0.3wt％を必要とするが、多すぎると被
削性を著しく劣化させるため2.0wt％を上限とする。Mn: 0.3wt% is required to improve the toughness of the base martensite by improving the hardenability of the steel and to improve the hardness and rolling fatigue life of the steel material. 2.0 wt% is set as the upper limit.
Cr:炭化物を形成し、高温転動疲労寿命特性を向上させ
るためには1.3wt％を必要とする。しかし多すぎると焼
戻後の硬度が低下し、かえって高温転動疲労寿命特性を
劣化させることから1.98wt％を上限とする。Cr: 1.3 wt% is required to form carbides and improve the high-temperature rolling fatigue life characteristics. However, if the content is too large, the hardness after tempering decreases and the high-temperature rolling fatigue life characteristics are rather deteriorated. Therefore, the upper limit is set to 1.98 wt%.
Mo:基地に固溶させることにより、焼戻後の硬度ならび
に転動疲労寿命特性を向上させることから0.3wt％を必
要とするが、さらに好ましくは0.5wt％を必要とする。
しかし多すぎてもその効果は認められず、コスト高とな
ることから、1.0wt％を上限とする。Mo: 0.3 wt% is required for improving the hardness after tempering and the rolling fatigue life characteristics by forming a solid solution in the matrix, but more preferably 0.5 wt%.
However, if the amount is too large, the effect is not recognized and the cost is increased. Therefore, the upper limit is 1.0 wt%.
Si＋Mo:高温焼戻後に優れた硬度と高温転動疲労寿命特
性を得るため1.0wt％以上を必要とする。Si + Mo: 1.0 wt% or more is required to obtain excellent hardness and high temperature rolling fatigue life characteristics after high temperature tempering.
W,V:高温で安定した炭化物を形成し高温転動疲労寿命特
性をさらに向上させる成分として、均しく有用な同効成
分であり、これらの含有量については、いずれも0.05wt
％より少ないと硬化がなく、また、0.5wt％より多いと
焼戻後の硬度が低下し、かえって高温転動疲労寿命特性
を劣化させるので、何れか一方のみ又は両者の併用の何
れの場合も0.05wt％以上0.5wt％以下の範囲とする。W, V: As a component that forms stable carbides at high temperatures and further improves the high-temperature rolling fatigue life characteristics, it is a uniformly effective component with the same effect.
%, There is no hardening, and if it is more than 0.5 wt%, the hardness after tempering is reduced, and the high-temperature rolling fatigue life characteristic is rather deteriorated. Therefore, in either case or in combination of both. The range is 0.05 wt% or more and 0.5 wt% or less.
Ni:基地に固溶し、焼戻後の硬度低下を抑制させるため
0.2wt％以上を含有することが望ましい。しかし多量に
含有させると、残留オーステナイトが多量に生成し焼戻
後の硬度を低下させることから、そのうれいのない2.0w
t％を上限とする。Ni: dissolves in the matrix and suppresses the decrease in hardness after tempering
It is desirable to contain 0.2 wt% or more. However, if contained in a large amount, since a large amount of retained austenite is generated and lowers the hardness after tempering, 2.0w
The upper limit is t%.
Cu:基地に固溶し、焼戻後の硬度低下を抑制させる点でN
iと同効であって0.1wt％以上含有することが望ましい
が、多すぎると鍛造性を劣化させるので、そのうれいの
ない1.0wt％を上限とする。Cu: N forms a solid solution in the matrix and suppresses a decrease in hardness after tempering.
Although it is the same effect as i and desirably contains 0.1 wt% or more, if it is too large, forgeability is deteriorated. Therefore, the upper limit is 1.0 wt%, which is not satisfactory.
次に、この発明の成分組成で特にCrならびにSi＋Moの
限定が重要で、その理由について以下に実験結果をもと
に説明を加える。Next, it is particularly important to limit the composition of Cr and Si + Mo in the composition of the present invention, and the reason will be described below based on experimental results.
表１は、C:1.0wt％、Mn:0.5wt％を含有する高炭素ク
ロム軸受鋼についてSi,Cr,及びMo量を変化させてそれぞ
れ溶製し、脱ガスのために真空脱ガス処理を施してから
熱間圧延により調整した試験材の、焼入を経た280℃焼
戻後の硬度と高温（180℃）転動疲労特性の測定結果を
示すものである。Table 1 shows that high-carbon chromium bearing steel containing 1.0 wt% C and 0.5 wt% Mn was melted with varying amounts of Si, Cr and Mo, and subjected to vacuum degassing for degassing. FIG. 3 shows the measurement results of hardness after quenching and 280 ° C. tempering and high temperature (180 ° C.) rolling fatigue characteristics of a test material prepared by hot rolling after application.
ここに転動疲労寿命特性は、スラスト形試験機を用い
て、一群の軸受を同条件で負荷回転しフレーキング（表
面はく離）による破損が10％に達するまでの総回転数を
求め表１の脚注※１に沿って対比評価した。Here, the rolling fatigue life characteristics were obtained by using a thrust type testing machine to calculate the total number of rotations until a group of bearings rotated under load under the same conditions and the damage due to flaking (surface peeling) reached 10%. Comparative evaluation was made along footnotes * 1.
表１に示す結果より、Crが1.3wt％以上のとき、Siが
0.5wt％未満で、かつMoが0.3wt％未満の場合（記号１及
び２）では、280℃焼戻後の硬度が不十分であり、高温
転動疲労寿命特性も劣り、また、Siが0.5wt％以上、あ
るいはMoが0.3wt％以上のいずれか一方が満足されてい
ない場合（記号８及び９）は、280℃焼戻後の硬度は十
分であるか、高温転動疲労寿命特性が劣り、さらに、Si
が0.5wt％以上で、Moが0.3wt％以上であっても、SiとMo
の合計で1.0wt％未満の場合（記号4,5及び６）並びにCr
が1.3wt％以下の場合（記号3,11及び17）は280℃焼戻後
で十分な硬度が得られるものの、優れた高温転動疲労寿
命特性を得ることができず、そしてSiが0.5wt％以上、M
oが0.3wt％以上であり、SiとMoの合計で1.0wt％以上で
あっても、Crが1.98wt％超えの場合（記号14及び20）に
は、280℃焼戻後の硬度が不十分であり、高温転動疲労
寿命特性も劣っている。 From the results shown in Table 1, when Cr is 1.3 wt% or more, Si
When the content is less than 0.5 wt% and the content of Mo is less than 0.3 wt% (symbols 1 and 2), the hardness after tempering at 280 ° C. is insufficient, the high-temperature rolling fatigue life characteristics are poor, and the content of Si is 0.5%. In the case where either wt% or more or Mo is 0.3 wt% or more is not satisfied (symbols 8 and 9), the hardness after tempering at 280 ° C is sufficient or the high-temperature rolling fatigue life characteristics are poor. , And Si
Is 0.5 wt% or more, and even if Mo is 0.3 wt% or more, Si and Mo
Of less than 1.0 wt% (symbols 4, 5 and 6) and Cr
Is less than 1.3 wt% (symbols 3, 11 and 17), although sufficient hardness can be obtained after tempering at 280 ° C, excellent high-temperature rolling fatigue life characteristics cannot be obtained, and Si is 0.5 wt%. % Or more, M
Even if o is 0.3 wt% or more and the sum of Si and Mo is 1.0 wt% or more, if Cr exceeds 1.98 wt% (symbols 14 and 20), the hardness after tempering at 280 ° C is not good. Sufficient and high-temperature rolling fatigue life characteristics are inferior.
一方、成分組成が、この発明の限定範囲にある場合
（記号7,10,12,13,15,16,18及び19）には、280℃焼戻後
で十分な硬度を示し、かつ高温転動疲労寿命特性も1.3
から2.2と優れた値を示している。On the other hand, when the component composition is within the limited range of the present invention (symbols 7, 10, 12, 13, 15, 16, 18, and 19), it shows sufficient hardness after tempering at 280 ° C and high temperature rolling. 1.3 dynamic fatigue life
From 2.2 to an excellent value.
（実施例） 転炉で溶製しRH脱ガス処理を施した後、連続鋳造で化
学成分を表２に示した多数のブルームを鋳造し、1240℃
の温度で30時間の拡散焼鈍を行った上で、直径が65φmm
の棒鋼に圧延した。(Example) After melting in a converter and performing RH degassing, a large number of blooms whose chemical components are shown in Table 2 were cast by continuous casting at 1240 ° C.
After 30 hours of diffusion annealing at a temperature of 65 mm
Rolled into steel bars.
ついで、上記棒鋼は、球状化焼鈍を施した後に、転動
疲労試験片の形状に加工し熱処理を加えた。焼入後の焼
戻温度を、記号Ａ鋼（SUJ2）については、180℃,260℃
で、記号E,I鋼については、240℃,260℃,300℃で、その
他の鋼については260℃でそれぞれ焼戻を行い、転動疲
労試験片を作製した。 Then, the steel bar was subjected to spheroidizing annealing, processed into a rolling fatigue test piece shape, and subjected to heat treatment. The tempering temperature after quenching is 180 ° C, 260 ° C for symbol A steel (SUJ2).
The symbols E and I were tempered at 240 ° C., 260 ° C. and 300 ° C., and the other steels were tempered at 260 ° C. to produce rolling fatigue test pieces.
転動疲労寿命試験には、スラスト型転動疲労寿命試験
機を用い、焼戻温度と疲労試験時の潤滑油温度の関係を
表３に示すごとくして疲労試験を行った。In the rolling fatigue life test, a thrust-type rolling fatigue life tester was used, and a fatigue test was performed with the relationship between the tempering temperature and the lubricating oil temperature during the fatigue test as shown in Table 3.
試験結果はワイブル分布に従うものと仮定して確率紙
上にまとめ、L10（累積破損確率が10％の時の、破損ま
での応力負荷回数）により、記号Ａ鋼（SUJ2）の180℃
焼戻材の潤滑油温度120℃における転動疲労寿命試験値
を１として対比評価した。 Test results are summarized in paper probability on the assumption that Weibull distribution, L 10 (cumulative damage probability when the 10% stress loading times to failure) by, 180 ° C. symbol A steel (SUJ2)
The rolling fatigue life test value at a lubricating oil temperature of 120 ° C. of the tempered material was set to 1 and compared.
上記評価値結果を硬度の測定結果とともに表４にまと
めて示す。Table 4 shows the results of the evaluation values together with the results of the hardness measurement.
記号Ａ（SUJ2）の従来鋼は、260℃焼戻材の、硬度はH
RC60未満と不十分であり、潤滑油温度180℃における転
動疲労寿命特性は0.2と劣っている。すなわち、同じ従
来鋼の180℃焼戻材の潤滑油温度120℃における転動疲労
寿命の1/5であることを示しており、この従来鋼SUJ2は
高温域（150℃から250℃）での使用は不適であることを
示している。 The conventional steel of symbol A (SUJ2) has a hardness of H
The RC is less than 60, which is insufficient, and the rolling contact fatigue life characteristic at a lubricating oil temperature of 180 ° C is inferior to 0.2. In other words, it shows that the rolling fatigue life of the same conventional steel at 180 ° C tempered material at rolling oil temperature of 120 ° C is 1/5 that of conventional steel SUJ2 in the high temperature range (150 ° C to 250 ° C). Use has been shown to be unsuitable.
記号B,J,L,Uの比較鋼は、それぞれC,V,W,Niなどの合
金元素の含有量が、この発明の限定範囲を逸脱したもの
であるが、260℃焼戻材の、硬度はHRC60未満と不十分で
あり、潤滑油温度180℃における転動疲労寿命特性はい
ずれも１未満と、従来鋼180℃焼戻材の潤滑油温度120℃
における転動疲労寿命くらべ劣っている。The comparative steels of symbols B, J, L, and U have the contents of alloying elements such as C, V, W, and Ni, respectively, which deviate from the limited range of the present invention. Hardness is less than HRC 60, which is insufficient. Rolling fatigue life characteristics at lubricating oil temperature of 180 ° C are all less than 1. Lubricating oil temperature of conventional steel 180 ° C tempered material is 120 ° C.
The rolling fatigue life is inferior to that of
一方、この発明鋼においては、焼戻温度260℃材にお
いてHRC60以上と十分な硬度が得られており、潤滑油温
度180℃での転動疲労寿命特性も１以上の値が得られて
いる。さらに、記号E,Iのこの発明鋼の焼戻温度240℃材
および300℃材においても十分な硬度と転動疲労寿命特
性（転動疲労試験時の潤滑油温度はそれぞれ150℃およ
び250℃）が得られている。On the other hand, in the steel of the present invention, a material having a tempering temperature of 260 ° C has a sufficient hardness of HRC 60 or more, and a rolling fatigue life characteristic at a lubricating oil temperature of 180 ° C has a value of 1 or more. I have. Furthermore, sufficient hardness and rolling fatigue life characteristics for the tempered 240 ° C and 300 ° C steels of the invention steels of symbols E and I (the lubricating oil temperature during the rolling fatigue test is 150 ° C and 250 ° C, respectively) Has been obtained.
また、W,Vの合金元素をそれぞれ単独あるいは複合し
て含有する記号I,K,M、そしてNi,Cuの合金元素をそれぞ
れ単独あるいは複合して含有する記号N,O,P、さらに
は、これらW,V,Ni,Cuの合金元素を２種類以上含有する
記号Q,R,S,Tなどの、この発明鋼は、焼戻温度260℃、潤
滑油温度180℃における転動疲労寿命特性は、全て2.0以
上の優れた値を示しており、これら合金元素の添加が有
効であることを示している。In addition, the symbols I, K, M containing the alloy elements of W and V alone or in combination, and the symbols N, O, P containing the alloy elements of Ni and Cu alone or in combination, respectively, The steel of the present invention, such as the symbols Q, R, S, and T containing two or more of these alloy elements of W, V, Ni, and Cu, has rolling fatigue life characteristics at a tempering temperature of 260 ° C and a lubricating oil temperature of 180 ° C. Indicate excellent values of 2.0 or more, indicating that the addition of these alloy elements is effective.
以上、この発明鋼は従来鋼SUJ2にくらべ使用許容温度
を高めることができ、使用許容温度250℃までの高温で
好適に使用することが可能である。As described above, the invention steel can increase the allowable use temperature as compared with the conventional steel SUJ2, and can be suitably used at a high use temperature of up to 250 ° C.
（発明の効果） この発明の耐熱軸受用鋼は、近年、自動車その他の分
野で、転がり軸受の高速化および高面圧化による温度上
昇が著しい使用環境にて、十分適用可能であって、製造
コストの増加が抑制されとくに安価に提供でき、今後広
い分野で有効に活用することができる。(Effect of the Invention) The heat-resistant bearing steel of the present invention is sufficiently applicable in recent years in the automotive and other fields, in a use environment where the temperature rise is remarkable due to the high speed and high surface pressure of the rolling bearing, and it is manufactured. The increase in cost can be suppressed, and it can be provided at a particularly low cost, and can be effectively used in a wide range of fields in the future.
フロントページの続き (72)発明者 田畑 綽久 千葉県千葉市川崎町１番地 川崎製鉄株 式会社技術研究本部内 (72)発明者 中野 昭三郎 千葉県千葉市川崎町１番地 川崎製鉄株 式会社技術研究本部内 (72)発明者 山下 政英 大阪府大阪市中央区南船場３丁目５番８ 号 光洋精工株式会社内 (72)発明者 柴田 正道 大阪府大阪市中央区南船場３丁目５番８ 号 光洋精工株式会社内 (72)発明者 竹中 幹夫 大阪府大阪市中央区南船場３丁目５番８ 号 光洋精工株式会社内 (56)参考文献 特公 昭54−41014（ＪＰ，Ｂ２)Continuing on the front page (72) Inventor Mikaru Tabata 1 Kawasaki-cho, Chiba-shi, Chiba Kawasaki Steel Corporation Research and Development Headquarters (72) Inventor Shozaburo Nakano 1 Kawasaki-cho, Chiba-shi, Chiba Kawasaki Steel Corporation Within the Research Headquarters (72) Inventor Masahide Yamashita 3-5-8 Minamisenba, Chuo-ku, Osaka City, Osaka Prefecture Inside (72) Inventor Masamichi Shibata 3-58-8 Minamisenba, Chuo-ku, Osaka City, Osaka Koyo Seiko (72) Inventor Mikio Takenaka 3-5-8 Minamisenba, Chuo-ku, Osaka-shi, Osaka Inside Koyo Seiko Co., Ltd.
Claims (4)
組成になる耐熱軸受用鋼。1. C: 0.8 wt% or more, 1.5 wt% or less, Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.3 wt% or more, 2.0 wt% or less, Cr: 1.3 wt% or more, 1.98 wt% % And Mo: 0.3wt% or more and 1.0wt% or less, and the total content of Si and Mo is 1.0wt% or more, with the balance being iron and unavoidable impurities. .
不可避不純物の組成になる耐熱軸受用鋼。2. C: 0.8 wt% or more, 1.5 wt% or less, Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.3 wt% or more, 2.0 wt% or less, Cr: 1.3 wt% or more, 1.98 wt% % And Mo: 0.3 wt% or more and 1.0 wt% or less, and a total of 1.0 wt% or more of Si and Mo, and W: 0.05 wt% or more and 0.50 wt% or less. And V: a heat-resistant bearing steel containing one or two selected from the group consisting of 0.05 wt% or more and 0.50 wt% or less, with the balance being iron and unavoidable impurities.
不可避不純物の組成になる耐熱軸受用鋼。C: 0.8 wt% or more, 1.5 wt% or less, Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.3 wt% or more, 2.0 wt% or less, Cr: 1.3 wt% or more, 1.98 wt% % And Mo: 0.3 wt% or more and 1.0 wt% or less, and the total of Si and Mo is 1.0 wt% or more, and Ni: 0.1 wt% or more and 2.0 wt% or less. And Cu: 0.05 wt% or more and 1.00 wt% or less, containing one or two selected from the following, with the balance being iron and unavoidable impurities.
及び不可避不純物の組成になる耐熱軸受用鋼。4. C: 0.8 wt% or more, 1.5 wt% or less, Si: 0.5 wt% or more, 2.0 wt% or less, Mn: 0.3 wt% or more, 2.0 wt% or less, Cr: 1.3 wt% or more, 1.98 wt% % And Mo: 0.3 wt% or more and 1.0 wt% or less, and a total of 1.0 wt% or more of Si and Mo, and W: 0.05 wt% or more and 0.50 wt% or less. And V: 0.05 wt% or more, 0.50 wt% or less, and one or more selected from: Ni: 0.1 wt% or more, 2.0 wt% or less, Cu: 0.05 wt% or more, 1.0 wt% or less, A heat-resistant bearing steel containing one or more selected from the group consisting of iron and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2047302A JP2724019B2 (en) | 1990-03-01 | 1990-03-01 | Heat-resistant bearing steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2047302A JP2724019B2 (en) | 1990-03-01 | 1990-03-01 | Heat-resistant bearing steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03253542A JPH03253542A (en) | 1991-11-12 |
| JP2724019B2 true JP2724019B2 (en) | 1998-03-09 |
Family
ID=12771491
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2047302A Expired - Fee Related JP2724019B2 (en) | 1990-03-01 | 1990-03-01 | Heat-resistant bearing steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2724019B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6402658B1 (en) | 1999-04-22 | 2002-06-11 | Koyo Seiko Co., Ltd. | Toroidal type continuously variable transmission |
| US7435308B2 (en) | 2005-05-27 | 2008-10-14 | Nsk Ltd. | Rolling bearing |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE10082695B4 (en) * | 1999-09-03 | 2007-05-31 | Nsk Ltd. | roller bearing |
| JP4616148B2 (en) * | 2005-10-18 | 2011-01-19 | 株式会社神戸製鋼所 | Bearing steel |
| US20070204940A1 (en) * | 2006-02-28 | 2007-09-06 | Jtekt Corporation | Rolling/sliding member, toroidal continuously variable transmission using the same method of manufacturing rolling/sliding member |
| JP4993486B2 (en) * | 2007-05-17 | 2012-08-08 | Ｎｔｎ株式会社 | Rolling member, rolling bearing, and rolling member manufacturing method |
| GB2513881B (en) * | 2013-05-08 | 2015-09-02 | Skf Ab | Steel alloy |
| JP7469596B2 (en) * | 2020-01-08 | 2024-04-17 | 日本製鉄株式会社 | Bearing Steel |
| JPWO2023054105A1 (en) * | 2021-09-28 | 2023-04-06 | ||
| WO2023095796A1 (en) * | 2021-11-24 | 2023-06-01 | 株式会社不二越 | Alloy steel for rolling bearing component; and rolling bearing component, raceway ring for rolling bearing, and rolling bearing using same |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS516116A (en) * | 1974-07-05 | 1976-01-19 | Nippon Special Steel Co Ltd | JIKUKEYOKO |
| JPS5672155A (en) * | 1979-11-16 | 1981-06-16 | Hitachi Ltd | Forged steel hardening work roll for hot finish rolling |
| JPS57210954A (en) * | 1981-06-22 | 1982-12-24 | Riken Corp | Alloy steel for piston ring |
-
1990
- 1990-03-01 JP JP2047302A patent/JP2724019B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6402658B1 (en) | 1999-04-22 | 2002-06-11 | Koyo Seiko Co., Ltd. | Toroidal type continuously variable transmission |
| US7435308B2 (en) | 2005-05-27 | 2008-10-14 | Nsk Ltd. | Rolling bearing |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH03253542A (en) | 1991-11-12 |
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