WO2022044392A1 - Élément coulissant et procédé de production de ce dernier - Google Patents

Élément coulissant et procédé de production de ce dernier Download PDF

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Publication number
WO2022044392A1
WO2022044392A1 PCT/JP2021/009318 JP2021009318W WO2022044392A1 WO 2022044392 A1 WO2022044392 A1 WO 2022044392A1 JP 2021009318 W JP2021009318 W JP 2021009318W WO 2022044392 A1 WO2022044392 A1 WO 2022044392A1
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WIPO (PCT)
Prior art keywords
layer
sliding member
carburized
member according
nitriding
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PCT/JP2021/009318
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English (en)
Japanese (ja)
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久光 波東
圭吾 中村
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株式会社日立製作所
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Publication of WO2022044392A1 publication Critical patent/WO2022044392A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races

Definitions

  • the present invention relates to a sliding member and a method for manufacturing the same.
  • sliding members In recent years, the usage environment of sliding members has been getting harsher. For example, in the aerospace field, high-speed rotation and use in high-temperature and low-temperature environments are required for weight reduction and performance improvement. In the consumer field, performance improvement by ultra-high speed rotation is required for vacuum cleaners, and in the machine tool field, high surface pressure that can withstand heavy cutting is required. Further, in the electric power field, high surface pressure is required to improve power generation efficiency in air volume power generation, and in the construction machinery field, low friction is required to improve the efficiency and operation response of hydraulic pump parts. In the automobile field, various sliding members are used, and there are all needs for high speed rotation, high surface pressure and low friction.
  • Damage near the surface of the member to be slid is mainly controlled by the following three types of damage.
  • the maximum shear stress of Hertz is generated at a deeper position as the acting load is larger, but considering the surface pressure range used in the current industrial field, it is the maximum at a depth of several tens of ⁇ m to several hundreds of ⁇ m from the surface. Become. Hardening at depths from tens of ⁇ m to hundreds of ⁇ m from the surface is important to increase durability against internal damage caused by the maximum shear stress of Hertz, and it is generally possible to harden from the surface to deep regions. Carburizing and induction hardening have been applied.
  • martensite produced by carburizing or induction hardening has higher frictional resistance and lower tempering softening resistance than the compound layer (nitriding layer) generated by nitriding described below.
  • the tempering and softening of the sliding portion due to the frictional heat generation of the sliding portion is suppressed as the frictional resistance is lower.
  • the compound layer produced by nitriding Fe 2-3 N ⁇ phase and Fe 4 N ⁇ ' is similar to the above reduction in frictional resistance. Phase) etc. are applied.
  • Patent Document 1 as a method of carburizing and nitriding a steel member, a Cr-containing steel member is carburized so as to have a carburizing concentration of 1.0% or more, and then only the carbide-forming layer on the surface layer of the steel member is subjected to carburizing treatment.
  • a method of subjecting a carburizing treatment and then quenching the steel member is disclosed.
  • the surface portion where high durability is required has low frictional resistance and is less likely to be tempered and softened.
  • the inside thereof has a hardened layer of several hundred ⁇ m or more.
  • the outermost surface of the layer, which has low friction and is less likely to be tempered and softened, and the hardened layer inside it are not completely separated layers, but are inclined layers in which the components of both are continuously changed. Is desirable.
  • the soaking treatment described in Patent Document 1 has a soaking concentration of about 0.3%. Further, in Patent Document 1, as an effect, in order to compensate for the decrease in hardenability due to the decrease in the amount of solid solution Cr in the surface layer portion as well as the increase in hardness, the hardness of the deep layer portion is obtained by subjecting only the surface layer portion to a nitriding treatment. Although it is described that the hardenability of the surface layer portion is improved while preventing the deterioration, there is room for improvement in terms of friction reduction on the outermost surface, temper softening resistance, peeling resistance and the like.
  • An object of the present invention is to provide a sliding member having a structure for suppressing internal damage, surface damage and softening damage in the vicinity of a surface, having low friction, and having high durability against high surface pressure.
  • the sliding member of the present invention has a structure in which a surface layer is formed on the outer surface region of the base material, and the surface layer is a nitride layer containing iron nitride having a nitrogen concentration of 5.9 to 11.1% on a mass basis. It contains a carburized layer located between the nitrided layer and the center of the base metal, and at least a part of the carburized layer is a martensite layer, and between the nitrided layer and the martensite layer, both are included.
  • a sloping layer is formed in which the concentrations of nitrogen and carbon, which are the components of the above, are continuously changing.
  • the method for manufacturing a sliding member of the present invention is a method for manufacturing a sliding member by forming a surface layer including a nitrided layer and a carburized layer in an outer surface region of the base material, and the base material is predetermined by high-frequency induction heating.
  • the nitriding layer includes a high-frequency treatment step of heating to the temperature of the above, a nitriding treatment step of supplying a nitriding gas to form a nitriding layer, and a carburizing step.
  • the carburized layer contains% iron nitride and is located between the nitrided layer and the center of the base metal, and at least a part of the carburized layer is a martenesite layer, between the nitrided layer and the martensite layer. Is formed with a sloping layer in which the concentrations of both components, nitrogen and carbon, are continuously changing.
  • a sliding member having a structure for suppressing internal damage, surface damage and softening damage in the vicinity of the surface, having low friction, and having high durability against high surface pressure.
  • FIG. 1 It is a transmission electron microscope image which shows the cross section of the test piece of Example 1.
  • FIG. 1 is a graph which shows the result of having analyzed the cross-sectional structure shown in FIG. 1 by the electron beam microanalyzer. It is an image which shows the result of phase identification of the cross-sectional structure shown in FIG. 1 by electron backscatter diffraction. It is a graph which shows the measurement result of the cross-sectional hardness of the test piece of Example 1.
  • FIG. It is a schematic diagram which shows the main part of the reciprocating sliding wear tester. It is a schematic diagram which shows the main part of the rolling fatigue tester. It is a flow figure which shows the manufacturing method of the sliding member of Example 1.
  • the present invention relates to a surface treatment technique for sliding members.
  • first processing method In the first step, the surface of the steel material is carburized at a temperature of about 900 ° C. to 1000 ° C. and cooled without quenching.
  • second step nitriding is performed to form a compound layer at a temperature of about 500 ° C to 580 ° C, and quenching is performed. In this case, since the quenching temperature is lower than the A1 transformation point, the carburized layer is not quenched and the hardness of the carburized layer becomes low.
  • the surface of the steel material is carburized at a temperature of about 900 ° C. to 1000 ° C. and quenched.
  • the carburized layer hardens due to quenching.
  • nitriding is performed to form a compound layer at a temperature of about 500 ° C to 580 ° C.
  • the carburized layer cured in the first step is tempered and softened.
  • the surface of the steel material is carburized at a temperature of about 900 ° C to 1000 ° C.
  • nitriding is performed to form a compound layer by cooling from a carburizing temperature of about 900 ° C. to 1000 ° C. to a nitriding temperature of about 500 ° C. to 580 ° C.
  • quenching is performed by heating to about the A1 transformation point or higher (for example, 830 ° C to 850 ° C). In this case, since the heating in the third step requires time for heating the furnace, nitrogen is released from the compound layer formed in the second step, and the compound layer disappears.
  • a nitride layer is formed on the outermost surface of the surface layer in the outer surface region of the base material.
  • the nitrided layer includes an ⁇ phase (Fe 2-3 N), a ⁇ 'phase (Fe 4 N), or a composite layer of an ⁇ phase and a ⁇ 'phase. These phases have the characteristics of low friction and high temper softening resistance.
  • a carburized layer is formed between the nitrided layer and the center of the base metal. At least a part of the carburized layer is a martensite layer (martensite structure).
  • the martensite layer is a hardened layer produced by carburizing and quenching and can withstand high surface pressure.
  • the martensite layer extends over several hundred ⁇ m.
  • an inclined layer is formed in which the concentrations of nitrogen and carbon, which are the components of both, are continuously changed.
  • the inclined layer has a structure having excellent peel resistance and high temper softening resistance.
  • the first method for constructing the above structure is to heat a carburized steel or a bearing steel carburized in carbon steel or the like by high frequency induction heating or energization heating in an atmosphere of nitride gas to a temperature equal to or higher than the A1 transformation point, for example. , 750 ° C to 850 ° C for several minutes or less, held for about 1 minute, a compound layer is formed on the outermost surface, and quenching is performed.
  • the A1 transformation point referred to here means the A1 transformation point of the carburized layer (the same applies hereinafter).
  • Nitrogen gas may be filled before heating or after being heated to about 750 ° C to 850 ° C.
  • nitriding at about 750 ° C. to 850 ° C. is not performed with a high nitriding potential, the diffusion of nitrogen becomes predominant, a compound layer having a high nitrogen concentration is not formed on the surface, and only an immersion layer having a low nitrogen concentration is formed. Not done.
  • ammonia which is a nitriding gas, in the range of 1 ⁇ 10 4 Pa to atmospheric pressure, and the concentration of ammonia is as high as 20% to 100%.
  • the temperature, ammonia pressure, and ammonia concentration have a range because there are suitable conditions for obtaining a compound layer in each combination of conditions.
  • the second method for constructing the above structure is to heat the carburized steel or the bearing steel carburized in carbon steel or the like by high frequency induction heating or energization heating in the atmosphere of nitride gas at 600 ° C. or higher and lower than the A1 transformation point. Heat to a temperature of several minutes or less, hold for about 1 to 30 minutes, form a compound layer on the outermost surface, and raise the temperature above the A1 transformation point, for example, about 800 ° C to 850 ° C, by high-frequency induction heating or energization heating. It has a step of heating in 1 minute or less and promptly quenching.
  • Nitrogen gas may be filled before heating or after being heated to a temperature of 600 ° C. or higher and lower than the A1 transformation point.
  • the temperature above the A1 transformation point for example, heating from 800 ° C. to 850 ° C. is not rapidly performed, the nitrogen in the compound layer is decomposed and released into the atmosphere. It is desirable to heat it in 1 minute or less because it may diffuse into the base material and deteriorate the properties of the compound layer or the compound layer may disappear.
  • nitriding at a temperature of 600 ° C. or higher and lower than the A1 transformation point is not carried out at a high nitriding potential, the diffusion of nitrogen becomes dominant, a compound layer having a high nitrogen concentration is not formed, and only an immersion layer having a low nitrogen concentration is formed. Not done.
  • nitriding at a high nitriding potential it is desirable to carry out nitriding of ammonia, which is a nitriding gas, in the range of 0.1 ⁇ 10 4 Pa to atmospheric pressure, and the concentration of ammonia is as high as 10% to 100%.
  • the temperature, ammonia pressure, and ammonia concentration have a range because there are suitable conditions for obtaining a compound layer in each combination of conditions.
  • the quenching process be performed at a temperature equal to or higher than the A1 transformation point of the carburized layer.
  • the quenching process be performed by heating to a temperature equal to or higher than the A1 transformation point.
  • the quenching step is performed by heating to a temperature equal to or higher than the A1 transformation point, it is desirable that the heating is performed at a heating rate that suppresses the decomposition of nitrogen in the nitrided layer.
  • the rate of temperature rise is preferably 100 ° C./min or higher.
  • test piece in this example was performed as follows.
  • a round bar test piece of chrome molybdenum steel SCM435 was used as a base material. This round bar test piece has a carbon concentration of about 0.35% and dimensions of 10 mm in diameter ⁇ 10 mm in length.
  • This round bar test piece is heated to 950 ° C in about 1 minute by high frequency induction heating, and the temperature is maintained. That is, the rate of temperature rise is 100 ° C./min or higher.
  • acetylene which is a carburized gas
  • a carburized layer was formed by vacuum carburizing.
  • the material on which the carburized layer is formed in this way may be referred to as a "carburized material”, and the material subjected to the carburized treatment as a pretreatment in this way may be referred to as a "base material".
  • the base metal does not need to be carburized to its center.
  • the carburized layer changed from the martensite layer to a depth of 1.0 mm or more from the outermost surface of the test piece. This provides durability against internal damage due to the maximum shear stress in Hertz.
  • FIG. 1 shows a transmission electron microscope image (TEM image) of the cross-sectional structure of the test piece obtained by the above treatment.
  • the cross section of the test piece has the following three layers. That is, the compound layer 1 (nitriding layer), the inclined layer 2, and the carburized layer 3.
  • the compound layer 1, the inclined layer 2, and the carburized layer 3 are laminated in order from the outermost surface on the outer surface region of the base metal, and these three layers form the surface layer.
  • FIG. 2 shows the results of analysis of the cross-sectional structure shown in FIG. 1 by an electron beam microanalyzer.
  • the two graphs shown in FIG. 2 show the concentration distribution of nitrogen and carbon.
  • an ⁇ phase (Fe 2-3 N) with a nitrogen concentration of about 8% is formed in the range from the outermost surface to a depth of about 7 ⁇ m, and the inner thickness is about about 7
  • a ⁇ 'phase (Fe 4 N) having a nitrogen concentration of about 5.9% is formed in the region of 1 ⁇ m.
  • the ⁇ phase and the ⁇ 'phase are the compound layer 1.
  • the nitrogen concentration is 11.1% in the case of Fe 2N and 7.7% in the case of Fe 3N .
  • the carbon concentration gradually increases in the range from about 8 ⁇ m to about 21 ⁇ m in depth.
  • the carbon concentration is almost constant (about 0.8%) inside the depth of about 25 ⁇ m.
  • the range from a depth of about 8 ⁇ m to about 21 ⁇ m is called the inclined layer 2, and the region deeper than that is called the carburized layer 3.
  • the surface layer contains a nitrided layer (compound layer 1) containing iron nitride having a nitrogen concentration of 5.9 to 11.1%, and is carburized located between the nitrided layer and the central portion of the base metal.
  • layer 3 the central portion of the base metal refers to the inner region of the test piece covered with the surface layer.
  • At least a part of the carburized layer 3 is a martensite layer.
  • the inclined layer 2 is a region formed between the nitrided layer and the martensite layer in which the concentrations of nitrogen and carbon, which are components of both (nitrided layer and martensite layer), are continuously changed. be. More specifically, the inclined layer 2 has a structure in which the nitrogen concentration decreases toward the center of the base metal and the carbon concentration increases toward the center of the base metal.
  • FIG. 3 shows the results of phase identification of the cross-sectional structure shown in FIG. 1 by electron backscatter diffraction.
  • an ⁇ phase (Fe 2-3 N), a ⁇ 'phase (Fe 4 N), and an ⁇ phase (ferrite) are formed from the outermost surface toward the inside.
  • FIG. 4 is a graph showing the measurement result of the cross-sectional hardness.
  • the horizontal axis is the distance (depth) from the outermost surface, and the vertical axis is the Vickers hardness Hv0.2 (hardness).
  • the hardness of the carburized layer is about 800 Hv near the surface, and the effective curing depth of 550 Hv or more is about 1 mm.
  • FIG. 7 collectively shows the processing process of the test piece in this embodiment, that is, the manufacturing method of the sliding member.
  • high frequency induction heating capable of heating a material such as a steel material to a predetermined temperature in a very short time is applied.
  • a vacuum carburizing treatment S120
  • a carburizing gas such as acetylene is supplied to increase the carbon concentration on the surface of the material.
  • a nitriding treatment S130
  • a nitriding gas such as ammonia is supplied to form a compound layer.
  • quenching (S140) and tempering (S150) are performed.
  • the round bar test piece was treated in the same manner as in Example 1 to form a carburized layer.
  • Example 1 In this example as well, the same structure and hardness as in Example 1 were confirmed.
  • FIG. 8 collectively shows the processing process of the test piece in this embodiment, that is, the manufacturing method of the sliding member.
  • high frequency induction heating capable of heating a material such as a steel material to a predetermined temperature in a very short time is applied.
  • a vacuum carburizing treatment S220
  • a carburizing gas such as acetylene is supplied to increase the carbon concentration on the surface of the material.
  • a nitriding treatment S230
  • a nitriding gas such as ammonia is supplied to form a compound layer.
  • induction hardening (S240) and tempering S250 are performed.
  • a round bar test piece of bearing steel SUJ2 was used as a base material.
  • This round bar test piece has a carbon concentration of about 1% and has dimensions of 10 mm in diameter ⁇ 10 mm in length.
  • this base material will be referred to as "bearing steel material”.
  • This round bar test piece was supplied with 100% ammonia gas, which is a nitride gas, to a pressure of 9 ⁇ 10 4 Pa, heated to 850 ° C. in about 1 minute by high frequency heating, and held for 1 minute to form a compound layer. did.
  • This process can be called a high frequency nitriding process.
  • the temperature rising rate in this case is 100 ° C./min or more. It can also be said that the nitriding treatment step is performed by using high frequency induction heating.
  • Example 1 In this example as well, the same structure and hardness as in Example 1 were confirmed.
  • a round bar test piece of bearing steel SUJ2 was used as a base material. This round bar test piece has a carbon concentration of about 1% and has dimensions of 10 mm in diameter ⁇ 10 mm in length.
  • This round bar test piece was supplied with 100% ammonia gas, which is a nitride gas, to a pressure of 6 ⁇ 10 4 Pa, heated to 630 ° C. in about 1 minute by high frequency heating, and held for 3 minutes to form a compound layer. did. Then, ammonia was exhausted, replaced with an inert gas, and then quenched by high-frequency heating. As a result, the carburized layer was organized into martensite. Tempering was carried out at 180 ° C. for 30 minutes.
  • ammonia gas which is a nitride gas
  • Example 1 In this example as well, the same structure and hardness as in Example 1 were confirmed.
  • the conventional method refers to a method of performing carburizing, nitriding or carburizing nitriding without using high frequency heating.
  • Example 2 The same round bar test piece as in Example 1 is heated to 950 ° C in about 60 minutes in a vacuum carburizing furnace, and the temperature is maintained. After reaching 950 ° C, acetylene, which is a carburized gas, is supplied, and the carburized layer is quenched by vacuum carburizing for about 5 hours so that the carbon concentration is 0.8% and the effective effect depth is 1 mm. Was formed.
  • Example 2 The same round bar test piece as in Example 1 is heated to 570 ° C in about 60 minutes in a nitriding furnace, and the temperature is maintained. After reaching 570 ° C., ammonia as a nitriding gas was supplied, and nitriding treatment was performed for about 3 hours so that the nitrogen concentration became about 8% to form a nitrided layer.
  • a round bar test piece similar to that in Example 1 is heated to 950 ° C. in about 60 minutes in a vacuum carburizing furnace, and the temperature is maintained. After reaching 950 ° C., acetylene, which is a carburizing gas, was supplied and vacuum carburized for about 5 hours so that the carbon concentration was 0.8% and the effective effect depth was 1 mm to form a carburized layer. .. Then, a mixed gas in which 5 mol% of ammonia, which is a nitride gas, was mixed with nitrogen was cooled to 850 ° C. in 1 hour while maintaining a pressure of 1 ⁇ 10 3 Pa to form a carburized nitrided layer. After that, quenching was performed.
  • the friction coefficient and seizure load were measured using a reciprocating sliding wear tester.
  • FIG. 5 is a schematic diagram showing a main part of the reciprocating sliding wear tester.
  • the friction test piece 4 and the friction test mating material 5 are installed and fixed in the testing machine.
  • Lubricating oil 6 is applied onto the friction test mating material 5, the friction test mating material 5 is raised, and the friction test mating material 5 is brought into contact with the friction test piece 4.
  • the friction test mating material 5 is heated to 80 ° C. with a heater to maintain the temperature. After the temperature reaches 80 ° C. and stabilizes, sliding 7 is started. Then, the load 8 is increased in 0.1 kN increments every 2 minutes, and the test is continued until seizure occurs. Friction resistance was measured during the test, and seizure was determined when the frictional resistance increased sharply.
  • Table 1 shows the test results of frictional resistance and seizure load.
  • FIG. 6 is a schematic diagram showing a main part of a rolling fatigue tester.
  • the rolling test piece 9 and the rolling test partner material 10 are installed in the testing machine and fixed.
  • the lubricating oil 6 is heated to 60 ° C. and poured over the contact portion between the rolling test piece 9 and the rolling test mating material 10.
  • the rolling test mating material 10 is rotated at 1000 RPM by a motor, the rolling test piece 9 is rotated at 800 RPM by another motor, and a load 8 is applied to the contact surface so that the surface pressure of the contact portion becomes 3 GPa. Add.
  • the rolling fatigue test is continued. Then, the test is stopped when significant pitching damage occurs in the contact portion, and the life is judged.
  • the determination of significant pitching damage is detected by a vibration sensor attached in the vicinity of the rolling test piece 9.
  • Table 2 shows the results of the rolling fatigue test.
  • the rolling fatigue life is shown as a ratio with the life of conventional nitriding as 1.
  • conventional carburizing is 5 times and conventional carburizing nitriding is 7 times.
  • Examples 1 and 2 are test pieces obtained by molding a material containing carbon (C) having a content of 0.2 to 0.6% and unavoidable impurities and the balance being iron (Fe) by powder metallurgy. When the same treatment as in the above was performed and the effect was confirmed, it was confirmed that the same effect as in Examples 1 and 2 was obtained.
  • C carbon
  • Fe iron
  • the base metal was formed by powder metallurgy.
  • the carbon concentration of the carburized layer of the carburized material is preferably 0.5% or more, and more preferably 0.7% or more.
  • the carbon concentration is preferably 2.0% or less, and more preferably 1.5% or less.
  • the nitrogen concentration of the nitrided layer is preferably 0.5% or more , and the upper limit value is preferably 11.1% or less, which corresponds to the case of Fe 2N.
  • the lower limit is more preferably 0.7% or more.

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Abstract

Élément coulissant qui présente une configuration dans laquelle une couche de surface est formée dans la région de surface externe d'un matériau de base ; la couche de surface comprenant une couche nitrurée qui contient du nitrure de fer ayant une concentration en azote de 5,9 % à 11,1 % sur une base de masse, tout en comprenant une couche de carburation qui est positionnée entre la couche nitrurée et la partie centrale du matériau de base ; au moins une partie de la couche de carburation étant une couche de martensite ; et une couche de gradient, dans laquelle les concentrations d'azote et de carbone sont modifiées en continu, étant formée entre la couche nitrurée et la couche de martensite, ledit azote et ledit carbone étant des composants de la couche nitrurée et de la couche de martensite. Par conséquent, la présente invention est apte à fournir un élément coulissant qui présente une configuration qui supprime un dommage interne au voisinage de la surface, des dommages de surface et des dommages de ramollissement, tout en ayant un faible frottement et une durabilité élevée en matière de pression de contact élevée.
PCT/JP2021/009318 2020-08-27 2021-03-09 Élément coulissant et procédé de production de ce dernier WO2022044392A1 (fr)

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006009145A (ja) * 2004-05-24 2006-01-12 Komatsu Ltd 転動部材およびその製造方法
JP2011111637A (ja) * 2009-11-25 2011-06-09 Ud Trucks Corp 鋼材の処理方法
WO2013084800A1 (fr) * 2011-12-06 2013-06-13 日本精工株式会社 Palier à roulement et procédé de fabrication de ce dernier
JP2016125133A (ja) * 2015-01-08 2016-07-11 日産自動車株式会社 耐焼付性に優れた浸炭部材
WO2017154964A1 (fr) * 2016-03-08 2017-09-14 アイシン・エィ・ダブリュ株式会社 Composant en acier, composant d'engrenage et procédé permettant de fabriquer un composant en acier
JP2019196540A (ja) * 2018-05-11 2019-11-14 山陽特殊製鋼株式会社 水素侵入環境下の転がり疲れ寿命に優れる軸受用鋼

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006009145A (ja) * 2004-05-24 2006-01-12 Komatsu Ltd 転動部材およびその製造方法
JP2011111637A (ja) * 2009-11-25 2011-06-09 Ud Trucks Corp 鋼材の処理方法
WO2013084800A1 (fr) * 2011-12-06 2013-06-13 日本精工株式会社 Palier à roulement et procédé de fabrication de ce dernier
JP2016125133A (ja) * 2015-01-08 2016-07-11 日産自動車株式会社 耐焼付性に優れた浸炭部材
WO2017154964A1 (fr) * 2016-03-08 2017-09-14 アイシン・エィ・ダブリュ株式会社 Composant en acier, composant d'engrenage et procédé permettant de fabriquer un composant en acier
JP2019196540A (ja) * 2018-05-11 2019-11-14 山陽特殊製鋼株式会社 水素侵入環境下の転がり疲れ寿命に優れる軸受用鋼

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