JP2000297345A - Steel for carburized bearing - Google Patents
Steel for carburized bearingInfo
- Publication number
- JP2000297345A JP2000297345A JP11106778A JP10677899A JP2000297345A JP 2000297345 A JP2000297345 A JP 2000297345A JP 11106778 A JP11106778 A JP 11106778A JP 10677899 A JP10677899 A JP 10677899A JP 2000297345 A JP2000297345 A JP 2000297345A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- present
- life
- bearing
- carburized bearing
- 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.)
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Abstract
Description
【0001】[0001]
【発明の属する技術分野】この発明は耐摩耗性と面疲労
強度及び転動寿命に優れた軸受を得ることのできる浸炭
軸受用鋼に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel for a carburized bearing from which a bearing having excellent wear resistance, surface fatigue strength and rolling life can be obtained.
【0002】[0002]
【従来の技術及び発明が解決しようとする課題】従来、
浸炭軸受用鋼としてJIS SCr420,SCM42
0に代表される肌焼鋼が用いられて来た。しかしながら
近年軸受の長寿命化の要求がますます高まっており、か
かる状況の下で転動疲労強度を向上させた浸炭軸受用鋼
が種々提案されている。2. Description of the Related Art
JIS SCr420, SCM42 as carburized bearing steel
Case hardening steels represented by 0 have been used. However, in recent years, there has been an increasing demand for longer bearing life, and under such circumstances, various steels for carburized bearings having improved rolling fatigue strength have been proposed.
【0003】鋼の転動疲労強度を向上させるための手段
として従来より鋼中の酸素含有量を低減したり、或いは
SiやCr等の合金元素を添加することが有望視され、
検討されている。またその他にもCu,Sb等を始めと
する種々の合金元素を添加することも効果があるとの報
告もなされている。[0003] As means for improving the rolling fatigue strength of steel, it has been considered promising to reduce the oxygen content in steel or to add alloying elements such as Si and Cr.
Are being considered. It has also been reported that the addition of various alloying elements such as Cu and Sb is effective.
【0004】しかしながらこれら合金元素の添加や増量
は疲労強度の向上に効果があるものの極端に低い疲労強
度を示すものがあってばらつきが大きく、そのため平均
寿命があまり向上しないのが実状である。また極端に低
い強度を示すものがあることから信頼性の点においても
問題があり、そこで寿命のばらつきが少なく、安定して
長寿命の得られる浸炭軸受用鋼が求められていた。However, although the addition and increase of the amount of these alloy elements are effective for improving the fatigue strength, some alloys exhibit extremely low fatigue strength and have large variations, so that the actual life is not so much improved. There is also a problem in terms of reliability because some steels exhibit extremely low strength. Therefore, there has been a demand for a carburized bearing steel which has a small variation in life and a stable long life.
【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目的とするところは、
寿命のばらつきが少なく、高い転動寿命特性を有する浸
炭軸受用鋼を提供することにある。而してこの目的を達
成するための請求項1の浸炭軸受用鋼は、重量%でC:
0.1〜0.4%,Si:0.4〜3.0%,Mn:
0.3〜1.5%,P:≦0.03%,S:≦0.03
%,Ni:0.25〜3.5%,Cr:0.3〜5.0
%,Al:0.005〜0.050%,Ti:≦0.0
03%,O:≦0.0015%,N:≦0.025%,
残部が実質上Feから成る合金組成を有し且つ長さが
0.5mm以上のアルミナクラスターの存在量が10
−3個/mm3以下であることを特徴とする。SUMMARY OF THE INVENTION The present invention has been made in view of such circumstances, and its object is to provide:
An object of the present invention is to provide a carburized bearing steel having a small variation in service life and high rolling life characteristics. In order to achieve this object, the steel for carburized bearing according to claim 1 comprises C:
0.1-0.4%, Si: 0.4-3.0%, Mn:
0.3-1.5%, P: ≦ 0.03%, S: ≦ 0.03
%, Ni: 0.25 to 3.5%, Cr: 0.3 to 5.0
%, Al: 0.005 to 0.050%, Ti: ≦ 0.0
03%, O: ≦ 0.0015%, N: ≦ 0.025%,
The remaining amount of alumina clusters having an alloy composition substantially consisting of Fe and having a length of 0.5 mm or more is 10
−3 / mm 3 or less.
【0006】請求項2のものは、重量%でC:0.1〜
0.4%,Si:0.4〜3.0%,Mn:0.3〜
1.5%,P:≦0.03%,S:≦0.03%,N
i:0.25〜3.5%,Cr:0.3〜5.0%,A
l:0.005〜0.050%,Ti:≦0.003
%,O:≦0.0015%,N:≦0.025%であっ
てMo,V,Nbの何れか1種又は2種以上をMo:
0.03〜2.5%,V:0.05〜1.0%,Nb:
≦0.1%の範囲で含有し、残部が実質上Feから成る
合金組成を有し且つ長さが0.5mm以上のアルミナク
ラスターの存在量が10 −3個/mm3以下であること
を特徴とする。According to a second aspect of the present invention, C: 0.1 to
0.4%, Si: 0.4-3.0%, Mn: 0.3-
1.5%, P: ≦ 0.03%, S: ≦ 0.03%, N
i: 0.25 to 3.5%, Cr: 0.3 to 5.0%, A
l: 0.005 to 0.050%, Ti: ≦ 0.003
%, O: ≦ 0.0015%, N: ≦ 0.025%
And any one or more of Mo, V and Nb is Mo:
0.03 to 2.5%, V: 0.05 to 1.0%, Nb:
≦ 0.1%, with the balance being substantially Fe
Alumina having an alloy composition and having a length of 0.5 mm or more
Raster abundance is 10 -3Pieces / mm3Must be
It is characterized by.
【0007】[0007]
【作用】本発明者は、転動疲労寿命を向上させるための
種々の合金元素の組合せについて検討した結果、Siと
Niを複合添加することと併せて破壊起点となるアルミ
ナクラスターを一定以下に規制することで、特に短寿命
で軸受が破損する現象を抑制でき、これにより寿命のば
らつきを小さくし得て、平均寿命を効果的に高め得るこ
とを知得し、本発明を完成させた。また併せてMo,
V,Nbの何れか1種又は2種以上を添加することで軸
受の平均寿命を更に効果的に高め得ることを知得した。The present inventor studied the combination of various alloying elements for improving the rolling fatigue life, and found that the combined addition of Si and Ni limits the alumina cluster which is a fracture starting point to a certain level or less. By doing so, it has been found that the phenomenon that the bearing is broken particularly with a short service life can be suppressed, whereby the variation in the service life can be reduced and the average service life can be effectively increased, and the present invention has been completed. In addition, Mo,
It has been found that the average life of the bearing can be more effectively increased by adding one or more of V and Nb.
【0008】次に本発明における各化学成分の限定理由
について詳述する。 C:0.1〜0.4% Cは軸受として必要な強度を得るとともに浸炭処理後に
十分な表面硬さを確保する上で0.1%以上必要であ
る。但し0.4%を超えると靭性並びに被削性が低下す
るので0.1〜0.4%の範囲とする。Next, the reasons for limiting each chemical component in the present invention will be described in detail. C: 0.1 to 0.4% C is required to be 0.1% or more in order to obtain necessary strength as a bearing and to secure sufficient surface hardness after carburizing. However, if it exceeds 0.4%, the toughness and machinability are reduced.
【0009】Si:0.4〜3.0% Siは焼入れマルテンサイト組織を緻密なものとし、鋼
の靭性や耐疲労特性を向上させる上で有効である。但し
0.4%より少ないとそうした効果が得られないので
0.4%以上含有させる。一方3.0%を超えると靭性
並びに加工性が劣化するので上限を3.0%とする。Si: 0.4 to 3.0% Si is effective in making the quenched martensite structure dense and improving the toughness and fatigue resistance of the steel. However, if the content is less than 0.4%, such effects cannot be obtained, so the content is made 0.4% or more. On the other hand, if it exceeds 3.0%, toughness and workability deteriorate, so the upper limit is made 3.0%.
【0010】Mn:0.3〜1.5% Mnは鋼の溶製時における脱酸並びに脱硫元素として作
用するとともに、鋼の焼入れ性を高める上で有効な元素
であり、そのために本発明では0.3%以上含有させ
る。但し1.5%を超えると加工性並びに被削性が劣化
するので上限を1.5%とする。Mn: 0.3 to 1.5% Mn acts as a deoxidizing element and a desulfurizing element at the time of smelting steel, and is an element effective in improving the hardenability of steel. 0.3% or more is contained. However, if it exceeds 1.5%, workability and machinability deteriorate, so the upper limit is made 1.5%.
【0011】P:≦0.03% S:≦0.03% P,Sは軸受の強度劣化の原因となる。そこで本発明で
はP,Sをそれぞれ0.03%以下に規制する。P: ≦ 0.03% S: ≦ 0.03% P and S cause deterioration of the strength of the bearing. Therefore, in the present invention, P and S are each regulated to 0.03% or less.
【0012】Ni:0.25〜3.5% Niは鋼の焼入れ性及び焼入れ・焼戻し後の靭性を向上
させるのに有効な元素であり、そのために本発明では
0.25%以上含有させる。但し3.5%を超えると鋼
の靭性及び加工性を低下させるので上限を3.5%とす
る。Ni: 0.25 to 3.5% Ni is an element effective for improving the hardenability of steel and the toughness after quenching and tempering. Therefore, in the present invention, Ni is contained in an amount of 0.25% or more. However, if it exceeds 3.5%, the toughness and workability of the steel are reduced, so the upper limit is made 3.5%.
【0013】Cr:0.3〜5.0% Crは鋼の焼入れ性及び焼入れ・焼戻し後の強度並びに
靭性を向上させるのに有効な元素で、そのために本発明
では0.3%以上含有させる。但し5.0%より多く含
有させると焼入れ性及び被削性を害するので上限を5.
0%とする。Cr: 0.3-5.0% Cr is an element effective for improving the hardenability of steel, the strength after quenching and tempering, and the toughness. Therefore, in the present invention, Cr is contained in an amount of 0.3% or more. . However, if the content is more than 5.0%, hardenability and machinability are impaired, so the upper limit is set to 5.
0%.
【0014】Al:0.005〜0.050% AlはAlNとなって結晶粒を微細化する効果があり、
そのため本発明ではAlを0.005%以上含有させ
る。但し0.050%を超えて多量に含有させると鋼の
清浄度が低下するとともに結晶粒の粗大化防止効果が却
って低下するため、上限を0.050%とする。Al: 0.005 to 0.050% Al becomes AlN and has an effect of refining crystal grains.
Therefore, in the present invention, 0.005% or more of Al is contained. However, if it is contained in a large amount exceeding 0.050%, the cleanliness of the steel is lowered and the effect of preventing the crystal grains from coarsening is rather lowered, so the upper limit is made 0.050%.
【0015】N:≦0.025% NはAlと結合してAlNを生成し結晶粒を微細化する
働きをする。但し多量に含有させると却って鋼の強度を
劣化させる。そこで本発明ではNの含有量の上限を0.
025%とする。より望ましい範囲は0.01〜0.0
2%である。N: ≦ 0.025% N combines with Al to form AlN and serves to refine crystal grains. However, if contained in a large amount, the strength of the steel is rather deteriorated. Therefore, in the present invention, the upper limit of the N content is set to 0.
025%. A more desirable range is 0.01 to 0.0
2%.
【0016】Ti:≦0.003% Tiは硬質析出物TiNを生成して転動疲労破壊の破壊
起点となり、疲労寿命低下の原因となる。そこで本発明
ではTiの含有量を0.003%以下に規制する。Ti: ≦ 0.003% Ti forms hard precipitate TiN and becomes a starting point of rolling fatigue fracture, which causes a reduction in fatigue life. Therefore, in the present invention, the content of Ti is restricted to 0.003% or less.
【0017】O:≦0.0015% Oは鋼の清浄度を低下させ、疲労寿命を劣化させる原因
となる。そこで本発明ではOの含有量を0.0015%
以下に規制する。O: ≦ 0.0015% O reduces the cleanliness of the steel and causes the fatigue life to deteriorate. Therefore, in the present invention, the content of O is 0.0015%
It is regulated as follows.
【0018】Mo:0.03〜2.5% Moは鋼の強度を向上させる上で有用な元素であり、そ
こで本発明では選択元素として添加する際に0.03%
以上含有させる。但し2.5%より多く含有させると焼
入れ性が低下すると同時に被削性も劣化するので上限を
2.5%とする。Mo: 0.03 to 2.5% Mo is a useful element for improving the strength of steel. Therefore, in the present invention, when adding Mo as a selective element, Mo is 0.03% to 2.5%.
It is contained above. However, if the content is more than 2.5%, the hardenability decreases and the machinability also deteriorates, so the upper limit is made 2.5%.
【0019】V :0.05〜1.0% Nb:≦0.1% V,Nbは結晶粒の微細化に寄与する元素であるが、含
有量が多過ぎると結晶粒微細化効果が小さくなるため、
これらを選択元素として添加する際にVについては0.
05〜1.0%,Nbについては0.1%以下の範囲で
含有させる。V: 0.05 to 1.0% Nb: ≤0.1% V and Nb are elements that contribute to the refinement of crystal grains. To become
When these are added as selective elements, V is set to 0.1.
And Nb in the range of 0.1% or less.
【0020】長さが0.5mm以上のアルミナクラスタ
ーの存在量が10−3個/mm3以下アルミナクラスタ
ーは疲労破壊の破壊起点となって疲労寿命のばらつき及
び平均寿命を低下させる原因となる。本発明者はこのア
ルミナクラスターの大きさ及び存在量について研究した
結果、長さが0.5mm以上のアルミナクラスターの存
在量を10−3個/mm3以下に規制することにより短
寿命で破壊する現象を効果的に抑制して寿命のばらつき
を抑え、また平均寿命を向上させ得ることを知得した。Alumina clusters having a length of 0.5 mm or more and having an abundance of 10 −3 / mm 3 or less become the starting point of fatigue fracture and cause variations in fatigue life and decrease in average life. The present inventor has studied the size and abundance of the alumina cluster. As a result, the alumina cluster having a length of 0.5 mm or more is broken down with a short life by regulating the abundance to 10 −3 / mm 3 or less. It has been found that the phenomenon can be effectively suppressed to suppress the variation in the service life and also to improve the average service life.
【0021】[0021]
【実施例】次に本発明の実施例を以下に詳述する。表1
に示す化学組成の浸炭軸受用鋼を溶製し、熱間圧延を行
って試験用の素材を得た。この素材から100mm×8
0mm×10mmの試験片を削り出し、周波数50MH
zの超音波を用いた全没水浸探傷を行い、深さ0.4m
mまでの領域のアルミナクラスターの粒度分布を測定し
た。Next, embodiments of the present invention will be described in detail. Table 1
A steel for a carburized bearing having the chemical composition shown in Table 1 was melted and hot-rolled to obtain a test material. 100mm x 8 from this material
A test piece of 0 mm x 10 mm was cut out and the frequency was 50 MH.
Total submerged immersion flaw detection using ultrasonic wave of z, depth 0.4m
The particle size distribution of the alumina cluster in the region up to m was measured.
【0022】[0022]
【表1】 [Table 1]
【0023】別に同じ素材から試験部直径12mmのラ
ジアル型転動疲労試験片を削り出し、図1に示す条件で
浸炭焼入れ・焼戻し処理を施した。但し実施例8のみは
浸炭温度1050℃とした。また焼戻し温度は、焼戻し
後の硬さがHRCで約62となるように図1の範囲内で
調整した。Separately, a radial rolling fatigue test specimen having a test portion diameter of 12 mm was cut out from the same material and carburized and quenched and tempered under the conditions shown in FIG. However, only in Example 8, the carburizing temperature was 1050 ° C. The tempering temperature was adjusted within the range of FIG. 1 so that the hardness after tempering was about 62 in HRC.
【0024】その後機械加工によって表面研磨を行い、
転動疲労試験に供した。ここで転動疲労試験は、ラジア
ル型転動疲労試験機によりSUJ2製ボールを用いて、
面圧5880MPa,試験温度室温の条件の下で行っ
た。表2に長さ0.5mm以上のアルミナクラスターの
単位体積当りの存在量及び転動疲労試験の結果を示して
いる。Thereafter, the surface is polished by machining,
The rolling fatigue test was performed. Here, the rolling fatigue test was performed using a SUJ2 ball with a radial rolling fatigue tester.
The test was performed under the conditions of a surface pressure of 5880 MPa and a test temperature of room temperature. Table 2 shows the amount of alumina cluster having a length of 0.5 mm or more per unit volume and the results of a rolling fatigue test.
【0025】[0025]
【表2】 [Table 2]
【0026】表2の結果から、SiとNiを複合添加し
且つ0.5mm以上の長さのアルミナクラスターの存在
量を10−3/mm3以下に規制して成る本発明例の場
合、Si,Ni及びアルミナクラスターの存在量が本発
明の条件を満たしていない比較例に比べて、転動寿命の
累積破損確率10%寿命(L10),同50%寿命(L
50)ともに良好であること、また特にMo,V,Nb
を更に添加して成る発明例8,11,12,13の場
合、それらL10,L50が著しく向上していることが
分かる。From the results in Table 2, it can be seen that, in the case of the present invention example in which Si and Ni are added in combination and the amount of alumina clusters having a length of 0.5 mm or more is regulated to 10 −3 / mm 3 or less. , Ni and alumina clusters do not satisfy the conditions of the present invention, as compared with the comparative example, in which the cumulative failure probability of the rolling life is 10% life (L 10 ) and 50% life (L 10 ).
50 ) Both are good, and especially Mo, V, Nb
It can be seen that in the case of Invention Examples 8, 11, 12, and 13 in which is further added, L 10 and L 50 are remarkably improved.
【0027】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
囲において種々変更を加えた形態で構成可能である。Although the embodiment of the present invention has been described in detail, this is merely an example, and the present invention can be configured in variously modified forms without departing from the gist thereof.
【0028】[0028]
【発明の効果】上記のように本発明によれば疲労寿命の
ばらつきが小さく、高い転動疲労強度を持つ浸炭軸受用
鋼を得ることができる。As described above, according to the present invention, it is possible to obtain a carburized bearing steel having a small variation in fatigue life and a high rolling fatigue strength.
【図1】本発明の実施例及び比較例の浸炭焼入れ・焼戻
し熱処理の処理条件を示す図である。FIG. 1 is a view showing processing conditions of carburizing, quenching and tempering heat treatments of Examples and Comparative Examples of the present invention.
Claims (2)
0.5mm以上のアルミナクラスターの存在量が10
−3個/mm3以下であることを特徴とする浸炭軸受用
鋼。C: 0.1-0.4% Si: 0.4-3.0% Mn: 0.3-1.5% P: ≦ 0.03% S: ≦ 0. 03% Ni: 0.25 to 3.5% Cr: 0.3 to 5.0% Al: 0.005 to 0.050% Ti: ≦ 0.003% O: ≦ 0.0015% N: ≦ 0 0.025% The amount of alumina clusters having an alloy composition substantially consisting of Fe and having a length of 0.5 mm or more is 10
-3 pieces / mm 3 or less steel carburized bearings, characterized in that.
有し且つ長さが0.5mm以上のアルミナクラスターの
存在量が10−3個/mm3以下であることを特徴とす
る浸炭軸受用鋼。2. C: 0.1-0.4% Si: 0.4-3.0% Mn: 0.3-1.5% P: ≦ 0.03% S: ≦ 0. 03% Ni: 0.25 to 3.5% Cr: 0.3 to 5.0% Al: 0.005 to 0.050% Ti: ≦ 0.003% O: ≦ 0.0015% N: ≦ 0 Mo: 0.03 to 2.5% V: 0.05 to 1.0% Nb: ≦ 0.1% Characterized in that the amount of alumina clusters having a length of 0.5 mm or more and an alumina cluster having a length of 0.5 mm or more is 10 −3 / mm 3 or less. .
Priority Applications (1)
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JP11106778A JP2000297345A (en) | 1999-04-14 | 1999-04-14 | Steel for carburized bearing |
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WO2008075889A1 (en) * | 2006-12-19 | 2008-06-26 | Seah Besteel Corporation | Ultra high strength carburizing steel with high fatigue resistance |
JP2010196107A (en) * | 2009-02-25 | 2010-09-09 | Nsk Ltd | Roller bearing |
EP2615190A1 (en) * | 2010-09-08 | 2013-07-17 | Nippon Steel & Sumitomo Metal Corporation | Bearing steel with excellent corrosion resistance, bearing parts, and precision machinery components |
CN109097682A (en) * | 2018-08-20 | 2018-12-28 | 盐城市联鑫钢铁有限公司 | A kind of high-strength fireproof reinforcing bar and preparation method thereof |
CN110438394A (en) * | 2019-04-29 | 2019-11-12 | 如皋市宏茂重型锻压有限公司 | A kind of high polishing pre-hardening mould steel and its preparation process |
CN111601908A (en) * | 2018-01-22 | 2020-08-28 | 日本制铁株式会社 | Carburized bearing steel member and steel bar for carburized bearing steel member |
-
1999
- 1999-04-14 JP JP11106778A patent/JP2000297345A/en not_active Withdrawn
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
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EP1574592A1 (en) * | 2002-12-12 | 2005-09-14 | Nippon Steel Corporation | Bearing steel excellent in workability and corrosion resistance, method for production thereof, and bearing member and method for manufacture thereof |
EP1574592A4 (en) * | 2002-12-12 | 2008-09-17 | Nippon Steel Corp | Bearing steel excellent in workability and corrosion resistance, method for production thereof, and bearing member and method for manufacture thereof |
WO2008075889A1 (en) * | 2006-12-19 | 2008-06-26 | Seah Besteel Corporation | Ultra high strength carburizing steel with high fatigue resistance |
JP2010196107A (en) * | 2009-02-25 | 2010-09-09 | Nsk Ltd | Roller bearing |
EP2615190A1 (en) * | 2010-09-08 | 2013-07-17 | Nippon Steel & Sumitomo Metal Corporation | Bearing steel with excellent corrosion resistance, bearing parts, and precision machinery components |
EP2615190A4 (en) * | 2010-09-08 | 2015-04-22 | Nippon Steel & Sumitomo Metal Corp | Bearing steel with excellent corrosion resistance, bearing parts, and precision machinery components |
CN111601908A (en) * | 2018-01-22 | 2020-08-28 | 日本制铁株式会社 | Carburized bearing steel member and steel bar for carburized bearing steel member |
CN111601908B (en) * | 2018-01-22 | 2022-04-26 | 日本制铁株式会社 | Carburized bearing steel member and steel bar for carburized bearing steel member |
CN109097682A (en) * | 2018-08-20 | 2018-12-28 | 盐城市联鑫钢铁有限公司 | A kind of high-strength fireproof reinforcing bar and preparation method thereof |
CN110438394A (en) * | 2019-04-29 | 2019-11-12 | 如皋市宏茂重型锻压有限公司 | A kind of high polishing pre-hardening mould steel and its preparation process |
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