JPH11293403A - Steel for bearing long service life and delayed fracture resistance and its production - Google Patents
Steel for bearing long service life and delayed fracture resistance and its productionInfo
- Publication number
- JPH11293403A JPH11293403A JP11593998A JP11593998A JPH11293403A JP H11293403 A JPH11293403 A JP H11293403A JP 11593998 A JP11593998 A JP 11593998A JP 11593998 A JP11593998 A JP 11593998A JP H11293403 A JPH11293403 A JP H11293403A
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- Prior art keywords
- steel
- less
- delayed fracture
- fracture resistance
- long
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Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、軸受や直動軸等、
高硬度状態で使用され鋼材や熱処理、使用中の環境から
侵入してくる水素に起因する遅れ破壊に優れた抵抗性を
有する軸受鋼及びその製造方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a bearing, a linear motion shaft, etc.
The present invention relates to a bearing steel used in a high hardness state and having excellent resistance to delayed fracture caused by a steel material, heat treatment, and hydrogen entering from an environment in use, and a method for producing the bearing steel.
【0002】[0002]
【従来の技術】遅れ破壊はボルト等、引張応力状態で使
用環境等から侵入する水素から発生し、調質硬さや合金
元素の調整等材料対策がとられることも多かったが、高
硬度の状態で使用される軸受などでは、遅れ破壊はあま
り問題にされなかった。しかし、最近熱処理や使用雰囲
気等から侵入する水素による早期破損が問題にされるよ
うになり、潤滑油の変更等が行われてはいるが、先に述
べたような材料は強度的にも引張強さが140〜150
kgf/mm2 硬さ換算で43〜45HRCに相当)といった
ところで、軸受等のような高荷重に耐えられるものでは
なく、耐遅れ破壊に優れた軸受材料からの対策が取られ
ることはなかった。2. Description of the Related Art Delayed fracture is generated from hydrogen invading from a service environment or the like in a tensile stress state such as a bolt, and material measures such as tempering hardness and adjustment of alloying elements are often taken. In the bearings used in the field, delayed fracture was not a serious problem. However, early breakage due to hydrogen entering from heat treatment or use atmosphere has recently become a problem, and although lubricating oil has been changed, such materials as described above have tensile strength. 140-150 strength
(equivalent to 43 to 45 HRC in terms of hardness in kgf / mm 2 ), the bearing cannot withstand a high load like a bearing or the like, and no countermeasures have been taken from a bearing material excellent in delayed fracture resistance.
【0003】[0003]
【発明が解決しようとする課題】本発明は、このような
用途に適した長寿命でかつ耐遅れ破壊特性に優れた軸受
用鋼を提供しようとするものであり、化学成分の最適化
とそれを可能にする製造方法を開発することにある。SUMMARY OF THE INVENTION An object of the present invention is to provide a bearing steel having a long life and excellent delayed fracture resistance suitable for such applications. To develop a manufacturing method that enables
【0004】[0004]
【課題を解決するための手段】発明者らは、軸受鋼にお
ける遅れ破壊挙動を鋭意研究するなかで、遅れ破壊の原
因となる鋼中の水素を微細なTi系析出物によりトラップ
させることにより、無効化させ遅れ破壊の抵抗性を上
げ、長寿命化が図られることを見出した。その場合、析
出物の粒子径は小さいほど水素をトラップする力が強
く、出来るだけ均一微細に分散を図ることが有効である
ことを見出した。しかし、添加量を上げるだけでは有効
な微細析出物は増加せず、粗大化して水素のトラップ力
が弱まり、また、応力集中元となり寿命特性等を逆に低
下させるようになり、添加量の最適化と鋼材を製造する
上での製造条件の最適化が必要であることが判った。Means for Solving the Problems While studying the delayed fracture behavior of bearing steel intensely, the inventors have found that hydrogen in steel that causes delayed fracture is trapped by fine Ti-based precipitates. It has been found that it can be invalidated to increase the resistance to delayed fracture and prolong the service life. In this case, it has been found that the smaller the particle diameter of the precipitate, the stronger the force for trapping hydrogen, and it is effective to disperse as uniformly and finely as possible. However, increasing the amount of addition alone does not increase the effective fine precipitates, but instead increases the coarsening, weakens the hydrogen trapping power, and also causes stress concentration to deteriorate the life characteristics and the like. It was found that it was necessary to optimize the production conditions for the production of steel and steel products.
【0005】すなわち上記の目的を達成する発明の手段
は、請求項1の発明では、重量割合で、C:0.65〜
1.2%、Si:0.05〜0.50%、Mn:0.2
〜2.0%、T1:0.05〜0.20%、Al:0.
005〜0.50%、N:0.0120%以下、O:2
0ppm以下、望ましくは10ppm以下、を含有し、
残部Fe及び不可避不純物とからなり、大きさ70nm
以下のTi炭化物、Ti炭窒化物を鋼中に微細分散させ
た優れた遅れ破壊抵抗性を有する長寿命軸受用鋼であ
る。[0005] That is, the means of the present invention for achieving the above object is, in the invention of claim 1, C: 0.65 to 0.65 by weight.
1.2%, Si: 0.05 to 0.50%, Mn: 0.2
To 2.0%, T1: 0.05 to 0.20%, Al: 0.
005 to 0.50%, N: 0.0120% or less, O: 2
0 ppm or less, desirably 10 ppm or less,
The balance consists of Fe and unavoidable impurities and has a size of 70 nm.
This is a long-life bearing steel having excellent delayed fracture resistance in which the following Ti carbide and Ti carbonitride are finely dispersed in steel.
【0006】請求項2の発明では、重量割合で、C:
0.65〜1.2%、Si:0.05〜0.50%、M
n:0.2〜2.0%、Ti:0.05〜0.20%、
Al:0.005〜0.050%、N:0.0120%
以下、O:20ppm以下、望ましくは10ppm以
下、を含有し、さらに、Ni:0.1〜2.0%、C
r:0.20〜2.0%、Mo:0.05〜1.0%の
中から選択した1種ないし2種以上を含有し、残部Fe
及び不可避不純物とからなり、大きさ70nm以下のT
i炭化物、Ti炭窒化物を鋼中に微細分散させた優れた
遅れ破壊抵抗性を有する長寿命軸受用鋼である。According to the second aspect of the present invention, C:
0.65 to 1.2%, Si: 0.05 to 0.50%, M
n: 0.2 to 2.0%, Ti: 0.05 to 0.20%,
Al: 0.005 to 0.050%, N: 0.0120%
In the following, O: 20 ppm or less, preferably 10 ppm or less, Ni: 0.1 to 2.0%, C
r: 0.20 to 2.0%, Mo: 0.05 to 1.0%, one or more selected from the group consisting of
And T of less than 70 nm
It is a long-life bearing steel having excellent delayed fracture resistance in which i carbide and Ti carbonitride are finely dispersed in steel.
【0007】請求項3の発明では、請求項1又は請求項
2の手段の長寿命軸受用鋼において、さらに合金成分と
して、重量割合でB:0.0005〜0.0050%含
有し、残部Fe及び不可避不純物とからなり、大きさ7
0nm以下のTi炭化物、Ti炭窒化物を鋼中に微細分
散させたことを特徴とする優れた遅れ破壊抵抗性を有す
る長寿命軸受用鋼である。According to a third aspect of the present invention, there is provided the long-life bearing steel according to the first or second aspect, further comprising B: 0.0005 to 0.0050% by weight as an alloying component, and the balance Fe And inevitable impurities, having a size of 7
A long-life bearing steel having excellent delayed fracture resistance, characterized in that Ti carbide and Ti carbonitride of 0 nm or less are finely dispersed in the steel.
【0008】請求項4の発明では、重量割合で、C:
0.65〜1.2%、Si:0.05〜0.50%、M
n:0.2〜2.0%、Ti:0.05〜0.20%、
Al:0.005〜0.050%、N:0.0120%
以下、O:20ppm以下、望ましくは10ppm以
下、を含有し、残部Fe及び不可避不純物とからなる鋼
材を1200〜1350℃の温度範囲に加熱・圧延し、
さらに同じ温度ないし800〜1050℃の温度で所定
の鋼材ないし部品に圧延ないし鍛造することにより、後
の熱処理工程で大きさ70nm以下のTi炭化物、Ti
炭窒化物を鋼中に微細分散させることにより優れた遅れ
破壊抵抗性を有する長寿命軸受用鋼を製造する方法であ
る。According to the invention of claim 4, C:
0.65 to 1.2%, Si: 0.05 to 0.50%, M
n: 0.2 to 2.0%, Ti: 0.05 to 0.20%,
Al: 0.005 to 0.050%, N: 0.0120%
Hereinafter, a steel material containing O: 20 ppm or less, desirably 10 ppm or less, and the balance consisting of Fe and inevitable impurities is heated and rolled to a temperature range of 1200 to 1350 ° C.,
Further, by rolling or forging a predetermined steel material or part at the same temperature or a temperature of 800 to 1050 ° C., a Ti carbide or Ti having a size of 70 nm or less is formed in a subsequent heat treatment step.
This is a method for producing a long-life bearing steel having excellent delayed fracture resistance by finely dispersing carbonitrides in the steel.
【0009】請求項5の発明では、重量割合で、C:
0.65〜1.2%、Si:0.05〜0.50%、M
n:0.2〜2.0%、Ti:0.05〜0.20%、
Al:0.005〜0.050%、N:0.0120%
以下、O:20ppm以下、望ましくは10ppm以
下、を含有し、さらに、Ni:0.1〜2.0%、C
r:0.20〜2.0%、Mo:0.05〜1.0%の
中から選択した1種ないし2種以上を含有し、残部Fe
及び不可避不純物とからなる鋼材を1200〜1350
℃の温度範囲に加熱・圧延し、さらに同じ温度ないし8
00〜1050℃の温度で所定の鋼材ないし部品に圧延
ないし鍛造することにより、後の熱処理工程で大きさ7
0nm以下のTi炭化物、Ti炭窒化物を鋼中に微細分
散させることにより優れた遅れ破壊抵抗性を有する長寿
命軸受用鋼を製造する方法である。According to the fifth aspect of the present invention, C:
0.65 to 1.2%, Si: 0.05 to 0.50%, M
n: 0.2 to 2.0%, Ti: 0.05 to 0.20%,
Al: 0.005 to 0.050%, N: 0.0120%
In the following, O: 20 ppm or less, preferably 10 ppm or less, Ni: 0.1 to 2.0%, C
r: 0.20 to 2.0%, Mo: 0.05 to 1.0%, one or more selected from the group consisting of
And 1200-1350 steel materials consisting of unavoidable impurities.
Heating and rolling to a temperature range of ℃, and then the same temperature to 8
By rolling or forging into a predetermined steel material or part at a temperature of 00 to 1050 ° C., a size of 7
This is a method for producing a long-life bearing steel having excellent delayed fracture resistance by finely dispersing Ti carbide and Ti carbonitride of 0 nm or less in steel.
【0010】請求項6の発明では、請求項4又は請求項
5の手段の長寿命軸受用鋼の製造方法における鋼材の合
金成分に、さらに重量割合でB:0.0005〜0.0
050%含有し、残部Fe及び不可避不純物とからなる
鋼材を1200〜1350℃の温度範囲に加熱・圧延
し、さらに同じ温度ないし800〜1050℃の温度で
所定の鋼材ないし部品に圧延ないし鍛造することによ
り、後の熱処理工程で大きさ70nm以下のTi炭化
物、Ti炭窒化物を鋼中に微細分散させたことを特徴と
する優れた遅れ破壊抵抗性を有する長寿命軸受用鋼の製
造方法である。According to a sixth aspect of the present invention, in the method of producing a long-life bearing steel according to the fourth or fifth aspect, the alloy component of the steel material further includes B: 0.0005 to 0.0 in a weight ratio.
A steel material containing 050% and the balance of Fe and unavoidable impurities is heated and rolled to a temperature range of 1200 to 1350 ° C, and further rolled or forged to a predetermined steel material or part at the same temperature to 800 to 1050 ° C. The present invention provides a method for producing a long-life bearing steel having excellent delayed fracture resistance, characterized in that Ti carbide and Ti carbonitride having a size of 70 nm or less are finely dispersed in steel in a subsequent heat treatment step. .
【0011】[0011]
【発明の実施の形態】この発明の実施の形態を実施例を
通じて記載する。この発明を実施するに当っての限定理
由について、まず、化学成分(以下、「重量割合」で示
す。)の限定理由について述べる。DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiments of the present invention will be described through examples. First, the reasons for limiting the chemical components (hereinafter, referred to as “weight ratios”) in carrying out the present invention will be described.
【0012】C:0.65〜1.2%について、Cは軸
受として必要な硬さを付与する元素であるが、0.65
%未満では軸受としての必要な硬さHRC59以上が得
られないことが有り、下限を0.65%とする。また、
1.2%を超えると凝固時に巨大炭化物や粗大なTi炭
窒化物が晶出しやすくなり、後工程でもその影響を取り
除くことが出来なくなるため、上限を1.2%とする。C: With respect to 0.65 to 1.2%, C is an element for imparting hardness necessary for a bearing.
%, The required hardness HRC59 or more as a bearing may not be obtained, and the lower limit is set to 0.65%. Also,
If it exceeds 1.2%, a giant carbide or coarse Ti carbonitride tends to crystallize during solidification, and it is not possible to remove the effect even in a later step, so the upper limit is made 1.2%.
【0013】Si:0.05〜0.50%について、S
iは脱酸剤や焼入性向上のために添加されるが、0.0
5%未満では脱酸効果が十分でなく、0.50%を超え
ると加工性が低下するため、下限を0.05%、上限を
0.50%とする。Si: 0.05-0.50%, S
i is added for the purpose of improving the deoxidizing property and hardenability.
If it is less than 5%, the deoxidizing effect is not sufficient, and if it exceeds 0.50%, the workability is reduced. Therefore, the lower limit is made 0.05% and the upper limit is made 0.50%.
【0014】Mn:0.2〜2.0%について、Mnも
Siと同様、脱酸材や焼入性向上のために添加される
が、0.20%未満では焼入性が不足し、2.0%を超
えると著しく加工性が低下するため、下限を0.20
%、上限を2.0%とする。Mn: For 0.2 to 2.0%, Mn is also added to improve the deoxidizing property and hardenability similarly to Si, but if it is less than 0.20%, the hardenability is insufficient. If the content exceeds 2.0%, the workability is significantly reduced.
%, And the upper limit is 2.0%.
【0015】Ti:0.05〜0.20%について、T
iはTi炭化物やTi炭窒化物として鋼中に微細分散す
ることによって、結晶粒度の微細化が図られ、マトリッ
クス強化により疲労特性、寿命特性の向上が図られる。
また、微細なTi炭化物やTi炭窒化物は、水素のトラ
ップサイトとして作用するため、水素の有害性を低下さ
せる。0.05%未満ではその効果が十分でなく、ま
た、0.20%を超えるとTi炭化物やTi炭窒化物が
粗大化して十分な効果を示さなくなるため、下限を0.
05%、上限を0.20%とする。Ti: 0.05 to 0.20%, T
i is finely dispersed in steel as Ti carbide or Ti carbonitride, whereby the crystal grain size is reduced, and the matrix characteristics are strengthened to improve fatigue characteristics and life characteristics.
In addition, fine Ti carbides and Ti carbonitrides act as trap sites for hydrogen, thereby reducing the harmfulness of hydrogen. If it is less than 0.05%, the effect is not sufficient, and if it exceeds 0.20%, Ti carbide or Ti carbonitride is coarsened and no sufficient effect is obtained.
05% and the upper limit is 0.20%.
【0016】Al:0.005〜0.050%につい
て、Alは脱酸剤として添加するが、0.005%未満
ではその効果が無く、また、0.050%を超えるとア
ルミナ系酸化物が増加して疲労強度や加工性を低下させ
るため、下限を0.005%、上限を0.050%とす
る。For Al: 0.005 to 0.050%, Al is added as a deoxidizing agent. If it is less than 0.005%, the effect is not obtained. The lower limit is set to 0.005% and the upper limit is set to 0.050% in order to increase the fatigue strength and the workability.
【0017】N:0.0120%以下について、Nは量
が多くなると粗大なTi窒化物、Ti炭窒化物として析
出するようになるため出来るだけ少ないほうが望まし
い。製造条件との関係から上限を0.0120%とす
る。With respect to N: 0.0120% or less, it is preferable that the N content is as small as possible because a large amount of N causes precipitation as coarse Ti nitride and Ti carbonitride. The upper limit is set to 0.0120% in relation to the manufacturing conditions.
【0018】O:20ppm以下について、Oは酸化物
系介在物として鋼中に存在し水素のトラップサイトとし
ての役割も考えられるが、むしろ粗大な析出物として、
疲労強度低下の役割が大きく、出来るだけ少ないほうが
望ましい。このため上限を20ppm、望ましくは10
ppmとする。O: At about 20 ppm or less, O is present in the steel as an oxide-based inclusion and may also serve as a hydrogen trap site, but rather as a coarse precipitate,
The role of lowering the fatigue strength is large, and it is desirable that it be as small as possible. Therefore, the upper limit is 20 ppm, preferably 10 ppm
ppm.
【0019】上記の成分の他に本発明鋼では、Ni、C
r、Moを単独あるいは複合して含有させることが出来
る。これらの作用は以下の通りである。In addition to the above-mentioned components, the steel of the present invention includes Ni, C
r and Mo can be contained alone or in combination. These actions are as follows.
【0020】Ni:0.1〜2.0%について、Niは
焼入性を向上させ、疲労強度、靱性等を向上させる。
0.1%未満ではその効果が十分でなく、2.0%を超
えると素材の軟化が困難になり加工性が著しく低下する
ため上限を2.0%とする。Ni: About 0.1 to 2.0%, Ni improves hardenability, and improves fatigue strength, toughness and the like.
If it is less than 0.1%, the effect is not sufficient, and if it exceeds 2.0%, the softening of the material becomes difficult and the workability is remarkably reduced, so the upper limit is made 2.0%.
【0021】Cr:0.20〜2.0%について、Cr
は焼入性や炭化物の球状化性を向上させ、疲労強度、靱
性等を向上させる。0.2%未満ではその効果が十分で
はなく、2.0%を超えると素材の軟化が困難になり加
工性が著しく低下するため上限を2.0%とする。Cr: 0.20 to 2.0%
Improves hardenability and spheroidization of carbides, and improves fatigue strength and toughness. If it is less than 0.2%, the effect is not sufficient, and if it exceeds 2.0%, the softening of the material becomes difficult and the workability is significantly reduced, so the upper limit is made 2.0%.
【0022】Mo:0.05〜1.0%について、Mo
は焼入性を向上させ、疲労強度、靱性等を向上させる。
0.05%未満ではその効果が十分ではなく、1.0%
を超えると素材の軟化が困難になり加工性が著しく低下
し、また上記の効果も飽和しコスト的にも不利になるた
め上限を1.0%とする。Mo: 0.05-1.0%, Mo
Improves hardenability and improves fatigue strength, toughness and the like.
If it is less than 0.05%, the effect is not sufficient, and 1.0%
If it exceeds 300, the softening of the raw material becomes difficult and the workability is remarkably reduced, and the above-mentioned effects are saturated and the cost is disadvantageous, so the upper limit is made 1.0%.
【0023】さらに上記の成分の他に本発明鋼では、B
を含有させることが出来る。この作用は以下の通りであ
る。In addition to the above components, the steel of the present invention
Can be contained. This operation is as follows.
【0024】B:0.0005〜0.0050%につい
て、Bは高周波焼入れ性を改善する元素として添加す
る。0.0005%未満ではその効果が十分ではなく、
0.0050%を超えると熱間加工性を低下させるよう
になるため上限を0.0050%とする。B: About 0.0005 to 0.0050%, B is added as an element for improving induction hardening. If it is less than 0.0005%, the effect is not enough,
If it exceeds 0.0050%, the hot workability will be reduced, so the upper limit is made 0.0050%.
【0025】上記の化学成分の鋼材を下記の条件で製造
した場合に、最も効果的な微細Ti系析出物が得られ、
優れた遅れ破壊特性と長寿命性を示すようになる。When a steel material having the above chemical composition is manufactured under the following conditions, the most effective fine Ti-based precipitate can be obtained.
It shows excellent delayed fracture characteristics and long life.
【0026】すなわち、上記の成分範囲に溶製した鋼を
鋼片ないし鋼材に圧延する場合に、1200〜1350
℃の温度範囲に加熱・圧延し、さらに同じ温度範囲ない
し更に低い800〜1050℃の温度範囲で所定の寸法
の鋼材に圧延ないし部品に鍛造することにより、後の焼
なましないし焼入焼戻し熱処理後でも、大きさ70nm
以下のTi炭化物、Ti炭窒化物を鋼中に微細分散させ
ることが出来、優れた遅れ破壊抵抗性を有する長寿命軸
受用鋼の製造方法を得ることが出来る。That is, when the steel melted in the above component range is rolled into a billet or a steel material, 1200 to 1350
C. and then forged into steel of a given size in the same temperature range or a lower temperature range of 800 to 1050 ° C. or forged into parts, so that it is not annealed or quenched and tempered. Even after, size 70nm
The following Ti carbides and Ti carbonitrides can be finely dispersed in steel, and a method for producing a long-life bearing steel having excellent delayed fracture resistance can be obtained.
【実施例】表1に示す化学成分の供試材を100kg真
空溶解炉で溶製し、1200〜1350℃の温度範囲
で、また、一部は同じ温度範囲及び800〜1050℃
の温度範囲で、さらに鍛伸して65mmφおよび30m
mφに仕上げた。さらに焼ならし、球状化焼なまし後試
験片に加工し、焼入焼戻しを施して最終使用状態にし
た。EXAMPLES 100 kg of test materials having the chemical components shown in Table 1 were melted in a vacuum melting furnace at a temperature in the range of 1200 to 1350 ° C, and partly in the same temperature range and 800 to 1050 ° C.
In the temperature range of 65mmφ and 30m
Finished to mφ. After normalizing and spheroidizing annealing, the test piece was processed, quenched and tempered, and finally used.
【0027】得られた鋼材につき、通常の清浄潤滑下と
0.5%の純水を含んだ潤滑下(水素侵入環境下)にお
けるスラスト寿命特性(試験片サイズ:60mm×40
mm×5mm)ならびに耐遅れ破壊性の目安として5%
塩酸浸漬による耐水素割れ感受性試験を行なった。With respect to the obtained steel material, thrust life characteristics under normal clean lubrication and under lubrication containing 0.5% pure water (under hydrogen intrusion environment) (test piece size: 60 mm × 40)
mm x 5mm) and 5% as a measure of delayed fracture resistance
A hydrogen cracking resistance test by immersion in hydrochloric acid was performed.
【0028】[0028]
【表1】 [Table 1]
【0029】表2に各供試材ごとの製造条件と析出物粒
子サイズおよび特性試験結果を示す。なお、製造条件で
圧延温度を2条件記入しているものは、2回に分けて鍛
伸を行なったものである。Table 2 shows the production conditions, precipitate particle size, and characteristic test results for each test material. In the case where the rolling conditions are described in two conditions in the manufacturing conditions, the forging was performed in two times.
【0030】[0030]
【表2】 [Table 2]
【0031】また、図1にスラスト寿命試験機の構造を
模式的に示し、表3に試験条件を示し、図2に水素割れ
感受性試験に用いた試験片の形状を示す。図1におい
て、1は試験片保持枠、2はスラスト試験片(60φ×
5〜10mm)、3は保持器、4は3/8インチ(9.
525mmφ)の鋼球、5は上部レース(#5130ス
ラスト軸受けレース)、6は回転軸(1200r.p.
m.)、7は潤滑油(#60スピンドル油)である。FIG. 1 schematically shows the structure of a thrust life tester, Table 3 shows test conditions, and FIG. 2 shows the shape of a test piece used in a hydrogen cracking susceptibility test. In FIG. 1, 1 is a test piece holding frame, 2 is a thrust test piece (60φ ×
5 to 10 mm), 3 is a cage, 4 is 3/8 inch (9.
525mmφ) steel ball, 5 is the upper race (# 5130 thrust bearing race), 6 is the rotating shaft (1200r.p.
m.) and 7 are lubricating oils (# 60 spindle oil).
【0032】[0032]
【表3】 [Table 3]
【0033】表2より、本発明鋼は水素侵入環境下での
寿命特性の低下が少なく、また、耐水素割れに対して高
い抵抗性を示し、遅れ破壊特性に優れていることが判
る。From Table 2, it can be seen that the steel of the present invention hardly deteriorates in life characteristics under a hydrogen intrusion environment, exhibits high resistance to hydrogen cracking resistance, and is excellent in delayed fracture characteristics.
【0034】[0034]
【発明の効果】以上説明したように、本発明は、Tiの効
果的添加と製造条件の最適化により、優れた遅れ破壊抵
抗性を有する長寿命軸受用鋼を提供することができる優
れた効果を有する。As described above, according to the present invention, it is possible to provide a long-life bearing steel having excellent delayed fracture resistance by effectively adding Ti and optimizing production conditions. Having.
【図1】スラスト寿命試験機の構造を模式的に示す図で
ある。FIG. 1 is a diagram schematically showing the structure of a thrust life tester.
【図2】水素割れ感受性試験の試験片形状を示す図であ
る。FIG. 2 is a view showing a test piece shape in a hydrogen cracking susceptibility test.
1 試験片保持枠 2 スラスト試験片 3 保持器 4 3/8インチ鋼球 5 上部レース 6 回転軸 7 潤滑油 DESCRIPTION OF SYMBOLS 1 Test piece holding frame 2 Thrust test piece 3 Cage 4 3/8 inch steel ball 5 Upper race 6 Rotation axis 7 Lubricating oil
Claims (6)
Si:0.05〜0.50%、Mn:0.2〜2.0
%、Ti:0.05〜0.20%、Al:0.005〜
0.50%、N:0.0120%以下、O:20ppm
以下を含有し、残部Fe及び不可避不純物とからなり、
大きさ70nm以下のTi炭化物、Ti炭窒化物を鋼中
に微細分散させたことを特徴とする優れた遅れ破壊抵抗
性を有する長寿命軸受用鋼。1. C: 0.65 to 1.2% by weight,
Si: 0.05 to 0.50%, Mn: 0.2 to 2.0
%, Ti: 0.05 to 0.20%, Al: 0.005 to
0.50%, N: 0.0120% or less, O: 20 ppm
Contains the following, the balance consisting of Fe and unavoidable impurities,
Long-life bearing steel having excellent delayed fracture resistance, characterized in that Ti carbide and Ti carbonitride having a size of 70 nm or less are finely dispersed in steel.
Si:0.05〜0.50%、Mn:0.2〜2.0
%、Ti:0.05〜0.20%、Al:0.005〜
0.050%、N:0.0120%以下、O:20pp
m以下を含有し、さらに、Ni:0.1〜2.0%、C
r:0.20〜2.0%、Mo:0.05〜1.0%の
中から選択した1種ないし2種以上を含有し、残部Fe
及び不可避不純物とからなり、大きさ70nm以下のT
i炭化物、Ti炭窒化物を鋼中に微細分散させたことを
特徴とする優れた遅れ破壊抵抗性を有する長寿命軸受用
鋼。2. C: 0.65 to 1.2% by weight,
Si: 0.05 to 0.50%, Mn: 0.2 to 2.0
%, Ti: 0.05 to 0.20%, Al: 0.005 to
0.050%, N: 0.0120% or less, O: 20pp
m or less, Ni: 0.1 to 2.0%, C
r: 0.20 to 2.0%, Mo: 0.05 to 1.0%, one or more selected from the group consisting of
And T of less than 70 nm
A long-life bearing steel having excellent delayed fracture resistance, characterized in that i-carbide and Ti carbonitride are finely dispersed in the steel.
用鋼において、さらに合金成分として、重量割合でB:
0.0005〜0.0050%含有し、残部Fe及び不
可避不純物とからなり、大きさ70nm以下のTi炭化
物、Ti炭窒化物を鋼中に微細分散させたことを特徴と
する優れた遅れ破壊抵抗性を有する長寿命軸受用鋼。3. The steel for a long-life bearing according to claim 1, wherein the alloy further contains B:
Excellent delayed fracture resistance characterized by containing 0.0005 to 0.0050%, the balance being Fe and unavoidable impurities, and finely dispersing Ti carbide and Ti carbonitride having a size of 70 nm or less in steel. Long-lasting bearing steel with high durability.
Si:0.05〜0.50%、Mn:0.2〜2.0
%、Ti:0.05〜0.20%、Al:0.005〜
0.050%、N:0.0120%以下、O:20pp
m以下を含有し、残部Fe及び不可避不純物とからなる
鋼材を1200〜1350℃の温度範囲に加熱・圧延
し、さらに同じ温度ないし800〜1050℃の温度で
所定の鋼材ないし部品に圧延ないし鍛造することによ
り、後の熱処理工程で大きさ70nm以下のTi炭化
物、Ti炭窒化物を鋼中に微細分散させたことを特徴と
する優れた遅れ破壊抵抗性を有する長寿命軸受用鋼の製
造方法。4. C: 0.65 to 1.2% by weight,
Si: 0.05 to 0.50%, Mn: 0.2 to 2.0
%, Ti: 0.05 to 0.20%, Al: 0.005 to
0.050%, N: 0.0120% or less, O: 20pp
m and a balance of Fe and inevitable impurities is heated and rolled to a temperature range of 1200 to 1350 ° C., and further rolled or forged to a predetermined steel material or part at the same temperature to a temperature of 800 to 1050 ° C. A method for producing a long-life bearing steel having excellent delayed fracture resistance, characterized in that Ti carbide and Ti carbonitride having a size of 70 nm or less are finely dispersed in the steel in a subsequent heat treatment step.
Si:0.05〜0.50%、Mn:0.2〜2.0
%、Ti:0.05〜0.20%、Al:0.005〜
0.050%、N:0.0120%以下、O:20pp
m以下を含有し、さらに、Ni:0.1〜2.0%、C
r:0.20〜2.0%、Mo:0.05〜1.0%の
中から選択した1種ないし2種以上を含有し、残部Fe
及び不可避不純物とからなる鋼材を1200〜1350
℃の温度範囲に加熱・圧延し、さらに同じ温度ないし8
00〜1050℃の温度で所定の鋼材ないし部品に圧延
ないし鍛造することにより、後の熱処理工程で大きさ7
0nm以下のTi炭化物、Ti炭窒化物を鋼中に微細分
散させたことを特徴とする優れた遅れ破壊抵抗性を有す
る長寿命軸受用鋼の製造方法。5. C: 0.65 to 1.2% by weight,
Si: 0.05 to 0.50%, Mn: 0.2 to 2.0
%, Ti: 0.05 to 0.20%, Al: 0.005 to
0.050%, N: 0.0120% or less, O: 20pp
m or less, Ni: 0.1 to 2.0%, C
r: 0.20 to 2.0%, Mo: 0.05 to 1.0%, one or more selected from the group consisting of
And 1200-1350 steel materials consisting of unavoidable impurities.
Heating and rolling to a temperature range of ℃, and then the same temperature to 8
By rolling or forging into a predetermined steel material or part at a temperature of 00 to 1050 ° C., a size of 7
A method for producing a long-life bearing steel having excellent delayed fracture resistance, characterized in that Ti carbide and Ti carbonitride of 0 nm or less are finely dispersed in the steel.
用鋼の製造方法における鋼材の合金成分に、さらに重量
割合でB:0.0005〜0.0050%含有し、残部
Fe及び不可避不純物とからなる鋼材を1200〜13
50℃の温度範囲に加熱・圧延し、さらに同じ温度ない
し800〜1050℃の温度で所定の鋼材ないし部品に
圧延ないし鍛造することにより、後の熱処理工程で大き
さ70nm以下のTi炭化物、Ti炭窒化物を鋼中に微
細分散させたことを特徴とする優れた遅れ破壊抵抗性を
有する長寿命軸受用鋼の製造方法。6. The steel component in the method for producing long-life bearing steel according to claim 4 or 5, further comprising 0.0005 to 0.0050% by weight of B in the alloy component of steel, the balance being Fe and unavoidable. 1200 to 13 steel materials consisting of impurities
It is heated and rolled to a temperature range of 50 ° C., and further rolled or forged into a predetermined steel material or part at the same temperature to a temperature of 800 to 1050 ° C., so that Ti carbide or Ti A method for producing a long-life bearing steel having excellent delayed fracture resistance, characterized by finely dispersing nitride in steel.
Priority Applications (1)
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JP11593998A JP3426495B2 (en) | 1998-04-09 | 1998-04-09 | Long-life bearing steel excellent in delayed fracture resistance and method of manufacturing the same |
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Application Number | Priority Date | Filing Date | Title |
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JP11593998A JP3426495B2 (en) | 1998-04-09 | 1998-04-09 | Long-life bearing steel excellent in delayed fracture resistance and method of manufacturing the same |
Publications (2)
Publication Number | Publication Date |
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JPH11293403A true JPH11293403A (en) | 1999-10-26 |
JP3426495B2 JP3426495B2 (en) | 2003-07-14 |
Family
ID=14674928
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010188834A (en) * | 2009-02-17 | 2010-09-02 | Jtekt Corp | Wheel bearing device |
JP2014025096A (en) * | 2012-07-25 | 2014-02-06 | Ntn Corp | Method for manufacturing bearing ring, bearing ring and rolling bearing |
KR101482364B1 (en) * | 2009-11-30 | 2015-01-13 | 제이에프이 스틸 가부시키가이샤 | Ingot for bearing, and process for producing bearing steel |
KR101482365B1 (en) * | 2009-11-30 | 2015-01-13 | 제이에프이 스틸 가부시키가이샤 | Bearing steel |
-
1998
- 1998-04-09 JP JP11593998A patent/JP3426495B2/en not_active Expired - Fee Related
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010188834A (en) * | 2009-02-17 | 2010-09-02 | Jtekt Corp | Wheel bearing device |
KR101482364B1 (en) * | 2009-11-30 | 2015-01-13 | 제이에프이 스틸 가부시키가이샤 | Ingot for bearing, and process for producing bearing steel |
KR101482365B1 (en) * | 2009-11-30 | 2015-01-13 | 제이에프이 스틸 가부시키가이샤 | Bearing steel |
JP2014025096A (en) * | 2012-07-25 | 2014-02-06 | Ntn Corp | Method for manufacturing bearing ring, bearing ring and rolling bearing |
Also Published As
Publication number | Publication date |
---|---|
JP3426495B2 (en) | 2003-07-14 |
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