JP2005042188A - Carbonitrided bearing steel with excellent rolling fatigue life under debris-contaminated environment - Google Patents
Carbonitrided bearing steel with excellent rolling fatigue life under debris-contaminated environment Download PDFInfo
- Publication number
- JP2005042188A JP2005042188A JP2003280211A JP2003280211A JP2005042188A JP 2005042188 A JP2005042188 A JP 2005042188A JP 2003280211 A JP2003280211 A JP 2003280211A JP 2003280211 A JP2003280211 A JP 2003280211A JP 2005042188 A JP2005042188 A JP 2005042188A
- Authority
- JP
- Japan
- Prior art keywords
- carbonitriding
- retained austenite
- rolling fatigue
- bearing steel
- amount
- 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.)
- Withdrawn
Links
Images
Classifications
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C2204/00—Metallic materials; Alloys
- F16C2204/60—Ferrous alloys, e.g. steel alloys
- F16C2204/62—Low carbon steel, i.e. carbon content below 0.4 wt%
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C2204/00—Metallic materials; Alloys
- F16C2204/60—Ferrous alloys, e.g. steel alloys
- F16C2204/74—Ferrous alloys, e.g. steel alloys with manganese as the next major constituent
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
Description
この本発明は異物混入潤滑環境下で優れた転動疲労寿命を有する浸炭窒化軸受鋼に関する。 The present invention relates to a carbonitrided bearing steel having an excellent rolling fatigue life in a lubricating environment containing foreign matter.
従来、機械構造部品等の軸受鋼としてJIS SUJ2,SCr420,SCM420等に代表される軸受鋼が用いられてきた。
しかしながら通常の軸受使用環境では長寿命を示すものでも、異物混入潤滑環境下では極端に寿命低下を生じることが知られている。
Conventionally, bearing steels represented by JIS SUJ2, SCr420, SCM420 and the like have been used as bearing steels for machine structural parts.
However, it is known that even if a normal bearing use environment shows a long service life, the service life is extremely reduced in a lubrication environment containing foreign matter.
代表的な例として、自動車のトランスミッションやデファレンシャルに用いられる軸受においてバリ,摩耗粉などの異物が潤滑油中に混入する。このためそのような個所に用いられる軸受の長寿命化には、異物混入環境下での使用に適した耐異物軸受鋼の開発が求められていた。 As a typical example, foreign matters such as burrs and wear powder are mixed in the lubricating oil in a bearing used in a transmission or a differential of an automobile. For this reason, in order to extend the life of bearings used in such places, development of foreign material bearing steels suitable for use in a foreign matter mixed environment has been demanded.
異物混入環境下では、混入異物による圧痕を起点とした表面起点型剥離が転動疲労寿命を支配する。
そこで寿命改善のためには圧痕の生成抑制、圧痕部の応力集中の低減、亀裂発生抵抗の向上等が効果があると考えられる。
そこでSUJ2鋼に浸炭窒化処理を施し、表面硬さ及び破壊抵抗を向上するとともに、表面残留オーステナイト量を増加し、圧痕による応力集中を緩和する方法がとられている。
In an environment where foreign matter is mixed, surface-origin type separation starting from an indentation due to the mixed foreign matter dominates the rolling fatigue life.
In order to improve the life, it is considered effective to suppress the generation of indentation, reduce the stress concentration in the indentation, and improve the resistance to crack generation.
Therefore, carbonitriding treatment is applied to SUJ2 steel to improve surface hardness and fracture resistance, increase the amount of retained austenite, and relieve stress concentration due to indentation.
しかしSUJ2,SCr420,SCM420鋼に浸炭窒化処理を施しても、異物混入環境下での転動疲労寿命はたかだか2〜3倍程度の向上に止まる。
近年軸受の使用環境はますます厳しくなってきており、そのような中で軸受のより一層の長寿命化が求められている。
However, even when carbonitriding is applied to SUJ2, SCr420, and SCM420 steel, the rolling fatigue life in an environment where foreign matter is mixed is only improved by about 2 to 3 times.
In recent years, the usage environment of bearings has become more severe, and in such a situation, the life of bearings has been required to be further extended.
異物混入環境下での転動疲労寿命を高めることを目的としたものとして、下記特許文献1に開示のものが従来公知である。
しかしながらこの特許文献1に開示のものは、高温環境下で使用される耐熱浸炭転がり軸受部品に関するもので、高温で使用される軸受にあっては高温焼戻しする必要があることから、そのような高温焼戻しをしても硬さが大幅に低下せず、また寸法安定性を確保できるようにしたものであって、本願発明とはその目的とするところが異なった別異のものである。
However, the one disclosed in
本発明はこのような事情を背景とし、異物混入環境下においてもSUJ2,SCr420,SCM420に代表される従来鋼に浸炭窒化処理をしたものに較べて更に優れた転動疲労寿命を有する浸炭窒化軸受鋼を提供することを目的としてなされたものである。 The present invention is based on such circumstances, and even in a foreign matter mixed environment, a carbonitriding bearing that has a better rolling fatigue life than conventional carbonitriding treatments such as SUJ2, SCr420, and SCM420. It was made for the purpose of providing steel.
而して請求項1のものは、重量%で、C:0.1〜0.4%,Si:≦1.0%,Mn:1.5超〜3%,P:≦0.03%,S:≦0.03%,Cr:0.3〜2.5%,Al:0.005〜0.050%,Ti:≦0.003%,O:≦0.0015%,N:≦0.025%,残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする。
Thus, the content of
請求項2のものは、請求項1に規定する合金成分に加え、更にNi,Moの何れか1種若しくは2種を重量%で、Ni:0.25〜3.5%,Mo:0.03〜2.5%で含有する組成を有し、残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする。
In addition to the alloy component defined in
請求項3のものは、請求項1,2の何れかに規定する合金成分に加え、更にVを重量%で、V:0.05〜1.0%で含有する組成を有し、残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする。
In addition to the alloy components defined in any one of
請求項4のものは、請求項1〜3の何れかに規定する合金成分に加え、更にNbを重量%で、Nb:≦0.1%で含有し、残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする。
In addition to the alloy components defined in any one of
かかる本発明は、SCr420鋼に代表される浸炭鋼をベースとして種々の合金元素の組合せについて検討した結果、適正な範囲でのMnの添加がMs点を下げて表面残留オーステナイト量を増加させる効果を有すること、またMnはそれ以外に単独で次の効果、即ちマトリックスの靭性を高め、切欠感受性を低減することにより異物混入環境下で生成する圧痕からの亀裂発生を抑制する働きをなすこと、更に浸炭窒化処理後若しくはその後の2次焼入れ焼戻し後において表面残留オーステナイト量を20〜50%としておくこと等の組合せによって、異物混入環境下での転動寿命が効果的に改善される知見を得、完成されたものである。 As a result of examining the combination of various alloy elements based on carburized steel represented by SCr420 steel, the present invention has the effect of adding Mn within an appropriate range to lower the Ms point and increase the amount of surface retained austenite. In addition, Mn has the following effect alone, that is, to increase the toughness of the matrix, and to reduce the notch sensitivity, thereby suppressing the occurrence of cracks from indentation generated in a foreign matter mixed environment, Obtaining knowledge that the rolling life in a foreign matter-contaminated environment is effectively improved by a combination of setting the surface retained austenite amount to 20 to 50% after carbonitriding or subsequent secondary quenching and tempering, It has been completed.
このような本発明によれば、従来に増して異物混入環境下で優れた転動疲労寿命を有する浸炭窒化軸受鋼を提供することができる。
本発明においては、上記に規定する合金成分に加え、必要に応じてNi,Moの1種若しくは2種をNi:0.25〜3.5%,Mo:0.03〜2.5%の範囲で含有させることができ(請求項2)、またVをV:0.05〜1.0%の範囲で(請求項3)、更にNbをNb:≦0.01%の範囲でそれぞれ含有させることができる(請求項4)。
これらによって、浸炭窒化軸受鋼の異物混入環境下での転動疲労寿命をより一層向上させることができる。
According to the present invention as described above, it is possible to provide a carbonitrided bearing steel having an excellent rolling fatigue life in an environment where foreign matter is mixed, as compared with the prior art.
In the present invention, in addition to the alloy components specified above, one or two of Ni and Mo can be included in the range of Ni: 0.25 to 3.5% and Mo: 0.03 to 2.5% as necessary ( (Claim 2) Further, V can be contained in a range of V: 0.05 to 1.0% (Claim 3), and Nb can be further contained in a range of Nb: ≦ 0.01% (Claim 4).
As a result, the rolling fatigue life of the carbonitrided bearing steel can be further improved in an environment where foreign matter is mixed.
次に本発明における各合金成分の限定理由を以下に詳述する。
C:0.1〜0.4%
Cは浸炭窒化処理後の芯部硬さに影響する。転がり軸受として必要な強度を得るために必要な芯部硬さを確保する上で、Cの含有量を0.1%以上にする必要がある。
但し、Cの含有量が0.4%を超えると靭性や熱間加工性ならびに被削性が低下するので、Cの含有量の上限値を0.4%とする。
Next, the reason for limitation of each alloy component in this invention is explained in full detail below.
C: 0.1-0.4%
C affects the core hardness after carbonitriding. In order to secure the core hardness necessary to obtain the strength required for a rolling bearing, the C content needs to be 0.1% or more.
However, if the C content exceeds 0.4%, the toughness, hot workability and machinability deteriorate, so the upper limit of the C content is set to 0.4%.
Si:≦1.0%
Siは鋼溶製時に脱酸作用を有するとともに、焼戻し軟化抵抗を向上させるので、それらのために含有する元素であるが、多くなると効果が飽和するとともに、鋼の変態点を上昇させるために熱処理温度を高くする必要が生じ、また鍛造性や被削性を低下させるのでその含有量の上限を1.0%とする。
Si: ≤1.0%
Si is a deoxidizing action during steel melting and improves tempering softening resistance, so it is an element contained for them, but when it increases, the effect is saturated and heat treatment is performed to raise the transformation point of steel. It is necessary to increase the temperature, and the forgeability and machinability are lowered, so the upper limit of the content is set to 1.0%.
Mn:1.5超〜3%
Mnは本発明にとって重要な成分であって、鋼のマルテンサイト変態の開始温度(Ms点)を下げ、焼入れ時の残留オーステナイトを増加し、また鋼の熱間加工性を高めるので、それらのために含有させる元素である。
Mnはまたマトリックスの靭性を高め、切欠感受性を低減することにより異物混入環境下で生成する圧痕からの亀裂発生を抑制し、転動疲労寿命を向上させる働きがある。
それらの作用効果を得るためには1.5%超含有させる必要があるが、多くなりすぎると素材の軟化焼鈍しが困難になるとともに、被削性も低下させるので、その含有量の上限を3%とする。
Mn: more than 1.5 ~ 3%
Mn is an important component for the present invention, which lowers the martensitic transformation start temperature (Ms point) of steel, increases the retained austenite during quenching, and increases the hot workability of the steel. It is an element to be contained in.
Mn also increases the toughness of the matrix and suppresses notch susceptibility, thereby suppressing the occurrence of cracks from indentations generated in the presence of foreign matter and improving the rolling fatigue life.
In order to obtain these effects, it is necessary to contain more than 1.5%. However, if the amount is too large, it will be difficult to soften and anneal the material, and the machinability will be reduced, so the upper limit of the content is 3%. And
P:≦0.03%
Pは鋼のオーステナイト粒界に偏析し、靭性や転動疲労寿命の低下を招くので0.03%以下とする必要がある。
P: ≤ 0.03%
P segregates at the austenite grain boundaries of the steel, leading to a decrease in toughness and rolling fatigue life. Therefore, P needs to be 0.03% or less.
S:≦0.03%
Sは鋼の熱間加工性を害し、鋼中で非金属介在物を形成して靭性や転動疲労寿命を低下させるので、その含有量を0.03%以下とする。
尚Sは前記のような有害な面をもつ反面、切削加工性を向上させる効果も有しているので、少なくすることが望ましいものの0.03%以下の範囲内で積極的に添加することもある。
S: ≤0.03%
S impairs the hot workability of steel and forms non-metallic inclusions in the steel to reduce toughness and rolling fatigue life. Therefore, its content is set to 0.03% or less.
Although S has the harmful side as described above, it also has an effect of improving the machinability, so it is desirable to reduce it, but it may be actively added within a range of 0.03% or less.
Cr:0.3〜2.5%
Crは焼入れ性の改善や焼戻し軟化抵抗の向上、寿命改善の効果を有する。これらの効果を得るためには0.3%以上が必要である。しかし2.5%を超えて添加すると、大型の炭化物が生成して転動疲労寿命を低下させてしまう。
Cr: 0.3-2.5%
Cr has the effect of improving hardenability, improving temper softening resistance, and improving life. In order to obtain these effects, 0.3% or more is necessary. However, if added over 2.5%, large carbides are formed and the rolling fatigue life is reduced.
Al:0.005〜0.050%
0.050%を超えてAlが多量に含有されると、硬質の酸化物系介在物を生成して顕著な転動疲労寿命の低下が生じる。なおAlはこのような問題点を有するものの、AlNを形成して結晶粒を微細化する効果もあるので、鋼の製造コストの上昇を招かない0.005%以上の範囲で含有させる。
Al: 0.005 to 0.050%
When a large amount of Al is contained exceeding 0.050%, hard oxide inclusions are generated, and the rolling fatigue life is significantly reduced. Although Al has such problems, it also has the effect of forming AlN to refine crystal grains, so it is contained in a range of 0.005% or more that does not increase the manufacturing cost of steel.
Ti:≦0.003%
Tiは窒化物を形成して非金属介在物となり、転動疲労破壊の起点となる可能性があるので、その含有量を0.003%以下に規制する。
Ti: ≦ 0.003%
Ti forms nitrides and becomes non-metallic inclusions, which may become the starting point of rolling fatigue failure. Therefore, the content is restricted to 0.003% or less.
O:≦0.0015%
Oは鋼中に酸化物を形成し、非金属介在物として転動疲労破壊の起点となる可能性があり、転動疲労寿命の低下を招くので、その含有量を0.0015%以下とする。
O: ≤ 0.0015%
O forms an oxide in the steel and may become a starting point for rolling fatigue failure as a non-metallic inclusion, leading to a decrease in rolling fatigue life, so its content is made 0.0015% or less.
N:≦0.025%
NはAlと結合してAlNを形成し、結晶粒を微細化させる効果を有している。しかし多量に含有させると却って鋼の強度を劣化させるので、Nの含有量の上限値を0.025%とする。
N: ≤ 0.025%
N combines with Al to form AlN and has the effect of refining crystal grains. However, if it is contained in a large amount, the strength of the steel is deteriorated, so the upper limit of the N content is set to 0.025%.
Ni:0.25〜3.5%
Niは焼入れ時の残留オーステナイト量を増加させるとともに焼入れ性を向上し、転動疲労過程での白色組織や炭化物組織の生成を抑制して軸受の寿命を長くするので、それらのために含有させる。その作用効果を得るためには0.25%以上含有させる必要があるが、多くなると効果が飽和するとともにコスト面で不利になるので含有量の上限値を3.5%とする。
Ni: 0.25-3.5%
Ni increases the amount of retained austenite at the time of quenching and improves the hardenability, and suppresses the formation of a white structure and a carbide structure during the rolling fatigue process, thereby extending the life of the bearing. In order to acquire the effect, it is necessary to contain 0.25% or more, but if it increases, since an effect will be saturated and it will become disadvantageous in terms of cost, let the upper limit of content be 3.5%.
Mo:0.03〜2.5%
Moは焼入れ時の残留オーステナイト量を増加させるとともに焼入れ性を向上させるので、それらのために含有させる。その作用効果を得るためには0.03%以上含有させる必要があるが、多くなると効果が飽和するとともにコスト面で不利になるので含有量の上限を2.5%とする。
Mo: 0.03-2.5%
Mo increases the amount of retained austenite at the time of quenching and improves the hardenability, so it is contained for them. In order to obtain the action effect, it is necessary to contain 0.03% or more, but if it increases, the effect is saturated and the cost becomes disadvantageous, so the upper limit of the content is set to 2.5%.
V:0.05〜1.0%
Vは炭化物を形成して軸受の耐磨耗性を向上させる働きがある。その作用効果を得るためには0.05%以上含有させる必要があるが、多くなり過ぎると巨大炭化物を生成して強度を低下させるので、その含有量の上限値を1.0%とする。
V: 0.05-1.0%
V has the function of forming carbides and improving the wear resistance of the bearing. In order to acquire the effect, it is necessary to contain 0.05% or more, but if it increases too much, a giant carbide is generated and the strength is lowered, so the upper limit of the content is set to 1.0%.
Nb:≦0.1%
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、0.1%以下の範囲で含有させる。
Nb: ≤0.1%
Nb is an element that contributes to the refinement of crystal grains. However, if the content is too large, the effect of crystal grain refinement is reduced, so it is contained in a range of 0.1% or less.
浸炭窒化処理後若しくは2次焼入れ後の表面硬さ:58HRC以上
軸受は、使用環境下での寸法を安定させるために使用環境温度以上の温度で焼戻し処理を施すのが一般的である。更に、異物混入下では異物の硬さより高い表面硬さを有することが転動寿命の向上に有効である。
また硬さが58HRC未満になると転動寿命が急激に低下する傾向があり、転動寿命のバラツキも大きくなる。そこで本発明では焼入れ焼戻し処理後の表面硬さを58HRC以上とする。
Surface hardness after carbonitriding or secondary quenching: 58 HRC or more Bearings are generally tempered at a temperature equal to or higher than the operating environment temperature in order to stabilize the dimensions in the operating environment. Further, it is effective for improving the rolling life to have a surface hardness higher than the hardness of the foreign matter when the foreign matter is mixed.
Further, when the hardness is less than 58 HRC, the rolling life tends to be abruptly reduced, and the variation in the rolling life is increased. Therefore, in the present invention, the surface hardness after quenching and tempering is set to 58 HRC or more.
表面残留オーステナイト量:20〜50%
表面残留オーステナイトは、異物混入環境下での転動疲労において靭性に優れているとともに、軸受として使用中にマルテンサイト変態し、その変態により高い加工硬化を生じることのみならず、表面残留オーステナイトが柔らかいために、異物によって生じる圧痕形状が繰返し負荷により変化するので、応力の集中を緩和する作用があり、疲労寿命を向上する効果がある。
Surface retained austenite amount: 20 to 50%
Surface-retained austenite is excellent in toughness in rolling fatigue under the environment where foreign matter is mixed, and not only does martensite transformation during use as a bearing and causes high work hardening due to the transformation, but also surface-retained austenite is soft. For this reason, since the shape of the indentation caused by the foreign matter is changed repeatedly by the load, there is an effect of relaxing stress concentration, and an effect of improving the fatigue life.
因みに図1は横軸に表面残留オーステナイト量を、縦軸にL10をとってそれらの関係を表したもので、この図1から明らかなように、表面残留オーステナイト量20〜50%の範囲でL10が良好な値を示している。
尚ここでL10は寿命を表す指標であって、累積破損確率が10%となる破損繰返し回数である。
上記の作用効果を得るためには、図1に示すように20%以上の表面残留オーステナイト量が必要である。しかし多過ぎると所定の焼入れ焼戻し硬さが得られないことにより、逆に疲労寿命が低下し、また軸受使用中に表面残留オーステナイトが分解することによる寸法変化も大きくなるので、その上限を50%とする。
FIG. 1 shows the relationship between the surface retained austenite amount on the horizontal axis and L 10 on the vertical axis. As is apparent from FIG. 1, the surface retained austenite amount is in the range of 20 to 50%. L 10 indicates a satisfactory value.
Here, L 10 is an index representing the life, and is the number of times of repeated damage at which the cumulative failure probability becomes 10%.
In order to obtain the above-described effects, a surface retained austenite amount of 20% or more is required as shown in FIG. However, if the amount is too large, the predetermined quenching and tempering hardness cannot be obtained, and conversely, the fatigue life is lowered, and the dimensional change due to the decomposition of the surface retained austenite during use of the bearing is increased. And
次に本発明の実施形態を以下に詳しく説明する。
表1に示す化学組成の軸受鋼を溶製し、熱間圧延鋼材を試験用の素材とした。
この素材から試験部直径63mmのスラスト型転動疲労試験片(図5中10)を削り出し、図2に示す条件(カーボンポテンシャルCP:0.8%)で浸炭処理を行った後、図3に示す条件で浸炭窒化処理を施した。
尚この浸炭窒化処理ではCP:1.1%,NH3:5%の条件で処理を行った。
Next, embodiments of the present invention will be described in detail below.
Bearing steel having the chemical composition shown in Table 1 was melted, and hot rolled steel was used as a test material.
A thrust type rolling fatigue test piece (10 in FIG. 5) having a test part diameter of 63 mm was cut out from this material, carburized under the conditions shown in FIG. 2 (carbon potential CP: 0.8%), and then FIG. Carbonitriding was performed under the conditions shown in FIG.
In this carbonitriding treatment, the treatment was performed under the conditions of CP: 1.1%, NH 3 : 5%.
この後、機械加工およびラッピング加工によって表面研磨を行い転動疲労試験に供した。
また一部試験片については同様に浸炭窒化処理した後、図4に示す条件で2次焼入れ焼戻し処理を行い、この後機械加工及びラッピング加工によって表面研磨を行い、転動疲労試験に供した。
Thereafter, the surface was polished by machining and lapping and subjected to a rolling fatigue test.
Further, some of the test pieces were similarly subjected to carbonitriding and then subjected to secondary quenching and tempering under the conditions shown in FIG. 4, followed by surface polishing by machining and lapping, and subjected to a rolling fatigue test.
なお、ここでは浸炭窒化処理を浸炭処理と浸炭窒化処理とに分けて行ったが、処理温度の適正化によって1回の処理で浸炭と浸炭窒化(つまり浸炭窒化処理)を行うことも可能である。 Although the carbonitriding process is divided into the carburizing process and the carbonitriding process here, carburizing and carbonitriding (that is, carbonitriding process) can be performed in one process by optimizing the processing temperature. .
同試験片のラッピング面をロックウェル硬さ計を用いて、5点平均でHRC表面硬さを測定した。
また、同ラッピング面より5mm角で厚さ1mmの試料をミクロカッターで切り出し、X線回析により表層の表面残留オーステナイト量を測定した。
The HRC surface hardness of the wrapping surface of the test piece was measured on a 5-point average using a Rockwell hardness meter.
Further, a 5 mm square sample having a thickness of 1 mm was cut from the lapping surface with a microcutter, and the amount of surface retained austenite on the surface layer was measured by X-ray diffraction.
転動疲労試験は、表2に示す条件で行った。具体的には異物として硬さ約750Hv,粒度100〜180μmに分級した高速度鋼ガスアトマイズ粉12を用いた。
またスラスト試験機14(図5参照)のハウジング16は内面に湾曲状の斜度を施し、試験中に異物撹拌が十分に行われ、転走面に適性に異物の噛込みが生じるように構成した。
The rolling fatigue test was performed under the conditions shown in Table 2. Specifically, high-speed steel gas atomized
In addition, the
表3に浸炭窒化処理した場合の、表4に浸炭窒化後に更に2次焼入れ焼戻し処理した場合の表面残留オーステナイト量、表面硬さ及び異物混入環境下での転動疲労寿命試験でのL10,L50寿命を示している。 Table 3 when carbonitriding, surface retained austenite amount in the case of further secondary quenching and tempering treatment after carbonitriding in Table 4, L 10 in rolling contact fatigue life test in surface hardness and under contaminated environment, L 50 Life is shown.
これらの結果に見られるように、浸炭窒化処理した場合、本発明例はMn添加の効果により比較例に較べて表面残留オーステナイト量は30%以上と高く、L10,L50寿命ともに優れている。 As can be seen from these results, when carbonitriding was performed, the amount of retained austenite in the example of the present invention was as high as 30% or more compared to the comparative example due to the effect of Mn addition, and both the L 10 and L 50 lifetimes were excellent. .
一方比較例23,45に示したようにMn量が3%を超えると(鋼種U)表面残留オーステナイト量は増加するが表面硬さの低下が大きく、L10,L50寿命も劣っている。 On the other hand, as shown in Comparative Examples 23 and 45, when the Mn amount exceeds 3% (Steel Type U), the surface retained austenite amount increases, but the surface hardness decreases greatly, and the L 10 and L 50 lifetimes are also inferior.
また、比較例17,18に示すように鋼種O,Pについて浸炭処理しただけの場合には、表面残留オーステナイト量は約30%ないしそれ以上であるにも拘わらず、L10,L50寿命は浸炭窒化した場合(発明例15,16)に較べて劣っている。
これは、窒素固溶による硬さ向上とともに、焼戻し軟化抵抗の改善及び表面残留オーステナイトの安定化によるものと考えられる。
なお、表1の鋼種QはJIS SCr420である。
Further, as shown in Comparative Examples 17 and 18, when the steel types O and P were only carburized, the L 10 and L 50 lifespans were obtained even though the surface retained austenite amount was about 30% or more. It is inferior to the case of carbonitriding (Invention Examples 15 and 16).
This is considered to be due to the improvement in hardness by nitrogen solid solution, the improvement in temper softening resistance and the stabilization of surface retained austenite.
The steel type Q in Table 1 is JIS SCr420.
本発明例において、浸炭窒化処理した後に2次焼入れを行った場合には、浸炭窒化処理だけの場合に比べて表面残留オーステナイト量はやや低下するものの表面硬さは上昇し、L10,L50寿命ともに優れている。 In the example of the present invention, when secondary quenching is performed after carbonitriding, the amount of surface retained austenite is slightly reduced compared to the case of only carbonitriding, but the surface hardness is increased, and L 10 , L 50 Both lifespan is excellent.
比較例でも浸炭窒化処理後に2次焼入れを行った場合は浸炭窒化処理だけの場合に比べてL10,L50寿命は優れるが、その向上程度は比較的小さく、本発明例の浸炭窒化処理だけの場合にも及ばない。 Even in the comparative example, when the secondary quenching is performed after the carbonitriding process, the L 10 and L 50 lifespan is superior to the case of only the carbonitriding process, but the improvement is relatively small, and only the carbonitriding process of the present invention example. This is not even the case.
以上本発明の実施の形態を詳述したがこれはあくまで一例示であり、本発明はその趣旨を逸脱しない範囲において種々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 variously modified forms without departing from the spirit of the present invention.
Claims (4)
C :0.1〜0.4%
Si:≦1.0%
Mn:1.5超〜3%
P :≦0.03%
S :≦0.03%
Cr:0.3〜2.5%
Al:0.005〜0.050%
Ti:≦0.003%
O :≦0.0015%
N :≦0.025%
残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする浸炭窒化軸受鋼。 % By weight
C: 0.1-0.4%
Si: ≤1.0%
Mn: more than 1.5 ~ 3%
P: ≤0.03%
S: ≦ 0.03%
Cr: 0.3-2.5%
Al: 0.005 to 0.050%
Ti: ≦ 0.003%
O: ≦ 0.0015%
N: ≦ 0.025%
It has a composition consisting of the balance inevitable impurities and Fe, the surface hardness after carbonitriding treatment or subsequent secondary quenching and tempering treatment is 58 HRC or more, and the amount of surface retained austenite is 20 to 50%. Carbonitrided bearing steel.
Ni:0.25〜3.5%
Mo:0.03〜2.5%
で含有する組成を有し、残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする浸炭窒化軸受鋼。 In addition to the alloy components defined in claim 1, either one or two of Ni and Mo in weight percent,
Ni: 0.25-3.5%
Mo: 0.03-2.5%
The surface hardness after the carbonitriding process or the subsequent secondary quenching and tempering process is 58 HRC or more, and the surface retained austenite amount is 20 to 20%. Carbonitrided bearing steel characterized by 50%.
V :0.05〜1.0%
で含有する組成を有し、残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする浸炭窒化軸受鋼。 In addition to the alloy components defined in any one of claims 1 and 2, and V in wt%,
V: 0.05-1.0%
The surface hardness after the carbonitriding process or the subsequent secondary quenching and tempering process is 58 HRC or more, and the surface retained austenite amount is 20 to 20%. Carbonitrided bearing steel characterized by 50%.
Nb:≦0.1%
で含有し、残部不可避的不純物及びFeからなる組成を有し、浸炭窒化処理若しくはその後の2次焼入れ焼戻し処理後の表面硬さが58HRC以上で、且つ表面残留オーステナイト量が20〜50%であることを特徴とする浸炭窒化軸受鋼。 In addition to the alloy components defined in any one of claims 1 to 3, Nb in weight percent,
Nb: ≤0.1%
And has a composition consisting of the balance inevitable impurities and Fe, the surface hardness after carbonitriding or subsequent secondary quenching and tempering is 58 HRC or more, and the amount of surface retained austenite is 20 to 50% Carbonitrided bearing steel characterized by that.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003280211A JP2005042188A (en) | 2003-07-25 | 2003-07-25 | Carbonitrided bearing steel with excellent rolling fatigue life under debris-contaminated environment |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003280211A JP2005042188A (en) | 2003-07-25 | 2003-07-25 | Carbonitrided bearing steel with excellent rolling fatigue life under debris-contaminated environment |
Publications (1)
Publication Number | Publication Date |
---|---|
JP2005042188A true JP2005042188A (en) | 2005-02-17 |
Family
ID=34266108
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2003280211A Withdrawn JP2005042188A (en) | 2003-07-25 | 2003-07-25 | Carbonitrided bearing steel with excellent rolling fatigue life under debris-contaminated environment |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP2005042188A (en) |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2008297618A (en) * | 2007-06-02 | 2008-12-11 | Sanyo Special Steel Co Ltd | Method for manufacturing carburized steel part excellent in indentation resistance |
JP2009204076A (en) * | 2008-02-27 | 2009-09-10 | Nsk Ltd | Rolling bearing |
KR100961040B1 (en) | 2008-04-28 | 2010-06-01 | 동아대학교 산학협력단 | Nitrided Steels having High Strength |
JP2010222697A (en) * | 2008-08-29 | 2010-10-07 | Sanyo Special Steel Co Ltd | Steel for machine structural use having excellent toughness |
JP2011168820A (en) * | 2010-02-17 | 2011-09-01 | Sumitomo Metal Ind Ltd | Steel product having carbo-nitrided layer and method for producing the same |
JP2012001774A (en) * | 2010-06-17 | 2012-01-05 | Kobe Steel Ltd | Case-hardening steel with little heat-treatment strain |
KR20120120000A (en) * | 2011-04-22 | 2012-11-01 | 가부시키가이샤 제이텍트 | Rolling sliding member, method of manufacturing the same, and rolling bearing |
WO2016017160A1 (en) * | 2014-07-29 | 2016-02-04 | 新日鐵住金株式会社 | Carbonitrided bearing member |
US9469883B2 (en) | 2009-05-13 | 2016-10-18 | Nippon Steel & Sumitomo Metal Corporation | Carburized steel part having excellent low cycle bending fatigue strength |
CN112501544A (en) * | 2020-08-27 | 2021-03-16 | 苏州新豪轴承股份有限公司 | Bearing part machining process |
-
2003
- 2003-07-25 JP JP2003280211A patent/JP2005042188A/en not_active Withdrawn
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2008297618A (en) * | 2007-06-02 | 2008-12-11 | Sanyo Special Steel Co Ltd | Method for manufacturing carburized steel part excellent in indentation resistance |
JP2009204076A (en) * | 2008-02-27 | 2009-09-10 | Nsk Ltd | Rolling bearing |
KR100961040B1 (en) | 2008-04-28 | 2010-06-01 | 동아대학교 산학협력단 | Nitrided Steels having High Strength |
JP2010222697A (en) * | 2008-08-29 | 2010-10-07 | Sanyo Special Steel Co Ltd | Steel for machine structural use having excellent toughness |
US9469883B2 (en) | 2009-05-13 | 2016-10-18 | Nippon Steel & Sumitomo Metal Corporation | Carburized steel part having excellent low cycle bending fatigue strength |
JP2011168820A (en) * | 2010-02-17 | 2011-09-01 | Sumitomo Metal Ind Ltd | Steel product having carbo-nitrided layer and method for producing the same |
JP2012001774A (en) * | 2010-06-17 | 2012-01-05 | Kobe Steel Ltd | Case-hardening steel with little heat-treatment strain |
KR20120120000A (en) * | 2011-04-22 | 2012-11-01 | 가부시키가이샤 제이텍트 | Rolling sliding member, method of manufacturing the same, and rolling bearing |
WO2016017162A1 (en) * | 2014-07-29 | 2016-02-04 | 新日鐵住金株式会社 | Steel for carbonitrided bearing |
WO2016017160A1 (en) * | 2014-07-29 | 2016-02-04 | 新日鐵住金株式会社 | Carbonitrided bearing member |
CN106574338A (en) * | 2014-07-29 | 2017-04-19 | 新日铁住金株式会社 | Carbonitrided bearing member |
JPWO2016017162A1 (en) * | 2014-07-29 | 2017-04-27 | 新日鐵住金株式会社 | Carbonitrided steel for bearings |
CN106661691A (en) * | 2014-07-29 | 2017-05-10 | 新日铁住金株式会社 | Steel for carbonitrided bearing |
JPWO2016017160A1 (en) * | 2014-07-29 | 2017-05-25 | 新日鐵住金株式会社 | Carbonitriding bearing parts |
CN106574338B (en) * | 2014-07-29 | 2018-07-10 | 新日铁住金株式会社 | Carbo-nitriding parts of bearings |
CN112501544A (en) * | 2020-08-27 | 2021-03-16 | 苏州新豪轴承股份有限公司 | Bearing part machining process |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5760453B2 (en) | Carburized material | |
JP5094126B2 (en) | Rolling and sliding parts and manufacturing method thereof | |
JP5202043B2 (en) | Rolling parts and manufacturing method thereof | |
JPWO2012077705A1 (en) | Gas carburized steel parts having excellent surface fatigue strength, steel for gas carburizing, and method for producing gas carburized steel parts | |
JP2007231305A (en) | Carburized component and carburized gear | |
KR20130004307A (en) | Steel component having excellent temper softening resistance | |
JP4923776B2 (en) | Rolling and sliding parts and manufacturing method thereof | |
JP2006322036A (en) | Vacuum-carburized parts and manufacturing method therefor | |
JP4283643B2 (en) | Bearing steel and bearing parts with excellent corrosion resistance | |
JP2005042188A (en) | Carbonitrided bearing steel with excellent rolling fatigue life under debris-contaminated environment | |
JP4847681B2 (en) | Ti-containing case-hardened steel | |
JP4343357B2 (en) | Rolling bearing parts for high temperature | |
JP2007113071A (en) | Case hardening steel having excellent rolling fatigue property and crystal grain coarsening prevention property | |
JP4569961B2 (en) | Manufacturing method of parts for ball screw or one-way clutch | |
JP2012140675A (en) | Case-hardening steel excellent in cold-workability, and high fatigue-resistant strength carburized material | |
JP7436779B2 (en) | Steel for carburized gears, carburized gears, and method for manufacturing carburized gears | |
JP4458592B2 (en) | Rolling bearing parts for high temperature | |
JP2003231943A (en) | Case hardening steel superior in temper softening resistance | |
JP7368697B2 (en) | Steel for carburized gears, carburized gears, and method for manufacturing carburized gears | |
JP3411387B2 (en) | Bearing member with excellent heat treatment productivity and delay characteristics of microstructure change due to repeated stress load | |
WO2000028102A1 (en) | High-temperature rolling bearing part | |
JP2004124215A (en) | Bearing steel of excellent rolling service life under environment with foreign matters mixed therein | |
JP4343356B2 (en) | Rolling bearing parts for high temperature | |
JP5361293B2 (en) | Carburized parts with excellent static strength | |
JP2008133501A (en) | Steel for gear to be vacuum-carburized |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20060526 |
|
A761 | Written withdrawal of application |
Free format text: JAPANESE INTERMEDIATE CODE: A761 Effective date: 20070528 |