US20100126632A1 - Manufacturing method for high-concentration carburized steel - Google Patents

Manufacturing method for high-concentration carburized steel Download PDF

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US20100126632A1
US20100126632A1 US12/447,914 US44791407A US2010126632A1 US 20100126632 A1 US20100126632 A1 US 20100126632A1 US 44791407 A US44791407 A US 44791407A US 2010126632 A1 US2010126632 A1 US 2010126632A1
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carburization
temperature
primary
steel
concentration
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Toshiyuki Morita
Masaomi Saruyama
Hiroyuki Tsuyuzaki
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Honda Motor Co Ltd
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Honda Motor Co Ltd
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Assigned to HONDA MOTOR CO., LTD. reassignment HONDA MOTOR CO., LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MORITA, TOSHIYUKI, SARUYAMA, MASAOMI, TSUYUZAKI, HIROYUKI
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/20—Carburising
    • C23C8/22—Carburising of ferrous surfaces
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium

Definitions

  • the present invention relates to a manufacturing method for high-concentration carburized steel and, more particularly, to a manufacturing method for high-concentration carburized steel in which fine and spherical carbides can be precipitated in a large amount in the surface thereof by carburization treatment.
  • high-concentration carburization a treatment of enhancing the carbon concentration in the vicinity of the surface of the material to precipitate carbides.
  • Materials obtained by the high-concentration carburization contains hard carbides dispersed in their structure, and hence they are characterized in that they have higher abrasion resistance and higher surface fatigue strength than those materials have which are obtained by conventionally performed eutectoid carburization.
  • patent document 1 discloses a method of carburization treatment of steel, which subjecting following steps on a machine structure member made of steel having C, 0.05-0.45%:
  • step (vi) subjecting third carburization by plasma carburization again at temperature still lower than the temperature of the secondary carburization by 10 to 60° C.; and then the step (iv) to thereby obtain a member in which the surface C concentration is 1.7% or more, in which the shape of the carbides in the carburized layer is approximately spherical, and which has excellent abrasion resistance and excellent pitching resistance.
  • carbides can be precipitated in a agglomerate shape at the austenite grain boundaries since carburization in the primary carburization is performed in a high density of C concentration exceeding Acm;
  • patent document 2 discloses a carburization heat treatment method of a steel member. The method includes:
  • the literature describes that fine carbides can be allowed to grow by retaining the carburized steel member in the temperature range of higher than the Ac 1 transformation temperature of the steel by 50° C. and lower than that by 150° C.
  • Non-patent document 1 Tetsuya Shimomura, Toshiyuki Morita, and Koichiro Inoue; DENKI-SEIKO (Electric Furnace Steel), vol. 77 (2006), p. 11
  • Patent document 1 Japanese Patent Examined Publication JP-B-2808621
  • Patent document 2 Japanese Patent unexamined publication JP-A-6-108226
  • the primary carburization treatment is performed mainly for the purpose of solid-dissolving carbon in a high concentration in the surface so as to precipitate fine carbides in a large amount upon re-heating for performing the secondary carburization treatment.
  • the secondary carburization treatment is performed mainly for the purpose of allowing fine carbides generated upon re-heating to grow. For such purposes, it is desirable that the difference in temperature between the primary carburization treatment and the secondary carburization treatment is large enough.
  • a problem that the invention is to solve is to provide a manufacturing method for high-concentration carburized steel, which enables dispersion of fine and spherical carbides in a large amount without shortening the furnace life.
  • Another problem that the invention is to solve is to provide a manufacturing method for high-concentration carburized steel, which does not cause large deformation after carburization treatment.
  • a further problem that the invention is to solve is to provide a manufacturing method for high-concentration carburized steel, which enables dispersion of fine and spherical carbides in a large amount without reducing working efficiency.
  • a still further problem that the invention is to solve is to provide a manufacturing method for high-concentration carburized steel, in which flake-like, coarse carbides are not precipitated at the grain boundaries, and which provides a high reproducibility of the structure.
  • the manufacturing method for high-concentration carburized steel of the invention includes:
  • the difference between the primary carburization temperature T 1 and the secondary carburization temperature T 2 can be made large enough even when the primary carburization temperature T 1 is a comparatively low temperature, by separating the secondary carburization treatment into a secondary carburization initial step of performing carburization at a secondary carburization temperature T 2 which is lower than the quenching temperature Tq and a secondary carburization late step of performing carburization at a quenching temperature Tq.
  • fine and spherical carbides can be dispersed in a large amount without shortening the furnace life and generating serious deformation after carburization treatment.
  • FIGS. 1A to 1D are schematic views showing change in structure in the case of performing high-concentration carburization under various conditions, and phase diagrams;
  • FIG. 2 is a view showing the typical carburization treatment pattern employed in Example.
  • a steel material to which the manufacturing method of the invention is applied contains alloy elements as described below, and the balance thereof is Fe and unavoidable impurities.
  • Kinds of the alloy elements, ranges of the components, and reasons for restricting the ranges are as follows.
  • the amount of C is small, ferrite is generated in the core portion, which reduces strength. Therefore, the amount of C is preferably 0.15 mass % or more.
  • the amount of C is preferably 0.30 mass % or less.
  • the amount of Si is small, tempered hardness of the matrix is reduced, which reduces strength. Therefore, the amount of Si is preferably 0.40 mass % or more.
  • the amount of Si is preferably 0.80 mass % or less.
  • the amount of Mn is preferably 0.3 mass % or more.
  • the amount of Mn is preferably 0.8 mass % or less.
  • the amount of Cr is small, the amount of generated carbides is reduced, which reduces strength. Also, ferrite is generated in the core portion, which reduces strength. Therefore, the amount of Cr is preferably 1.25 mass % or more.
  • the amount of Cr is 2.00 mass % or less.
  • the manufacturing method for high-concentration carburized steel of the invention includes a primary carburization step, a cooling step, a secondary carburization initial step, a secondary carburization late step, and a quenching step.
  • the primary carburization step is a step of carburizing a steel material having the above-described composition at a primary carburization temperature T 1 (° C.) so that the surface carbon concentration C becomes Ceu ⁇ C ⁇ C(Acm).
  • the primary carburization temperature T 1 is temperature higher than the secondary carburization start temperature T 2 s to be described hereinafter by 100° C. or more. In general, as the primary carburization temperature T 1 becomes higher, carburization to a predetermined carbon concentration can be achieved in a shorter time. To be specific, the primary carburization temperature T 1 is preferably 900° C. or higher.
  • the primary carburization temperature T 1 is preferably 1,100° C. or lower, more preferably 1,000° C. or lower.
  • the surface carbon concentration C of a steel material becomes Ceu ⁇ C ⁇ C(Acm).
  • surface carbon concentration means an average carbon concentration within the region of 10 ⁇ m from the surface.
  • Ceu means an eutectoid carbon concentration of a steel material containing Si, Mn, and Cr in the above-described ranges, respectively. With every above-described steel material, the eutectoid carbon concentration is 0.5 mass % or more.
  • C(Acm) means a carbon concentration corresponding to the Acm line of a steel material containing Si, Mn, and Cr in the above-described ranges, respectively, at the primary carburization temperature T 1 .
  • C ⁇ C(Acm) means to perform the primary carburization at temperature at which the surface temperature of the steel material becomes the Acm line or higher (i.e., temperature at which the surface becomes a single phase of ⁇ -phase).
  • the primary carburization must be performed so that the surface carbon concentration C can become larger than Ceu.
  • the carbon concentration C of the surface becomes excessive, carbides would be generated at the grain boundaries during the primary carburization. Since carbides generated in the primary carburization remain as such, generation of coarse carbides must be prevented. Specifically, absence of coarse carbides of 5 ⁇ m or more in long diameter is preferred. Therefore, the primary carburization must be performed so that the surface carbon concentration C can become C(Acm) or less.
  • C(Acm) becomes from about 1.25 to about 1.4 mass % when the primary carburization temperature T 1 is from 950 to 1,000° C.
  • the carburization method upon performing the primary carburization is not particularly limited, and various methods may be employed.
  • gas carburization and vacuum carburization are preferred as the carburization methods since handling is easy and treating period is short.
  • the surface carbon concentration C can be controlled within the above-described range by optimizing the carburizing conditions.
  • carburization is performed by heating a steel material in an atmosphere of a carburizing gas.
  • the amount of carburization can be controlled through carbon potential of the carburizing atmosphere.
  • Carbon potential is the surface equilibrium carbon concentration of pure iron equilibrated with the atmosphere and is dependent upon the CO/CO 2 ratio and the amount of H 2 O in the atmosphere.
  • the surface carbon concentration can be increased in a shorter time when the carbon potential becomes higher and/or when the primary carburization temperature T 1 becomes higher.
  • carburization can be performed by, for example, reducing the pressure inside the furnace into which a steel material has been introduced to about 1.3 Pa, and then heating to the carburization temperature with introducing thereinto a hydrocarbon gas such as methane or propane.
  • a hydrocarbon gas such as methane or propane.
  • the amount of carburization can be controlled through the time of introducing the hydrocarbon gas.
  • the carbon concentration in the vicinity of the surface may become too high. In such case, it is general to perform diffusion treatment of stopping supply of the hydrocarbon gas after carburization and retaining in the same state.
  • the cooling step is a step of cooling, after completion of the primary carburization step, the steel material at a cooling rate of 1° C./min or more to 700° C. or lower.
  • the steel material After completion of the primary carburization, the steel material is once cooled to temperature of 700° C. or lower.
  • the reason for cooling to temperature of 700° C. or lower is that, upon re-heating in the secondary carburization, fine carbides be precipitated within grains.
  • the cooling rate when the cooling rate is too slow, flake-like, coarse carbides are formed at the grain boundaries during cooling, thus too slow cooling rate is not preferred.
  • the coarse carbides generated during cooling will not disappear in the step to be described hereinafter, and can cause reduction of strength of the steel material. Therefore, the cooling rate of 1° C./min or more is preferred. A faster cooling rate is more preferred.
  • the secondary carburization initial step is a step wherein the temperature of the cooled steel material is raised to the secondary carburization start temperature T 2 s and the steel material is carburized at the secondary carburization temperature T 2 .
  • second carburization start temperature T 2 s means the temperature which satisfies the condition of the following formula (1).
  • the temperature difference between the secondary carburization start temperature T 2 s and the primary carburization temperature T 1 is preferably 100° C. or more. If the temperature difference therebetween is less than 100° C., there is the possibility of generation of flake-like, coarse carbides at the grain boundaries. A larger temperature difference therebetween is more preferred.
  • the secondary carburization start temperature T 2 s must be equal to, or higher than, Ac 1 point and must be equal to, or lower than, the Acm line temperature corresponding to the surface carbon concentration of a steel material immediately after initiation of the secondary carburization.
  • second carburization temperature T 2 means the temperature which satisfies the conditions of the following formula (2).
  • the secondary carburization temperature T 2 may be the same as the secondary carburization start temperature T 2 s or may be temperature higher than that.
  • the retaining time at the secondary carburization temperature T 2 may be such that, when the temperature is raised to the quenching temperature Tq to be described hereinafter, the surface temperature of the steel material does not exceed the Acm line temperature.
  • the surface carbon concentration increases as the time of retaining at the secondary carburization temperature T 2 is prolonged, and hence carburization can be performed with keeping the surface temperature of the steel material at Acm line or less.
  • the retaining time at the secondary carburization temperature T 2 is preferably 15 minutes or longer.
  • the secondary carburization temperature T 2 may be reached by raising the temperature stepwisely or continuously from the secondary carburization start temperature T 2 s.
  • stepwisely means to repeat the procedures of retaining the temperature at a definite level for a predetermined time, then raising the temperature with a predetermined temperature width, and retaining the temperature at the predetermined temperature for a predetermined time.
  • stepwisely raising the temperature carburization can be performed with retaining the surface temperature of the steel material at Acm line or less by optimizing the temperature-raising width and the temperature-retaining time.
  • the term “continuously” means to raise the temperature at a predetermined temperature-raising rate.
  • carburization can be performed with retaining the surface temperature of the steel material at Acm line or less by optimizing the temperature-raising rate.
  • the secondary carburization late step is a step of subsequently raising, after completion of the secondary carburization initial step, the temperature of the steel material up to the quenching temperature Tq (° C.), and further performing carburization at the quenching temperature Tq, provided that Tq ⁇ Acm line temperature (° C.) corresponding to the surface carbon concentration of the aforesaid steel material.
  • the secondary carburization late step is a step of not only raising the temperature of the steel material to the quenching temperature Tq but also adjusting the surface carbon concentration to an intended carbon concentration in a short time without precipitation of flake-like, coarse carbides at the grain boundaries. Therefore, the quenching temperature Tq must be equal to, or less than, the Acm line temperature corresponding to the surface carbon concentration of the steel material.
  • the temperature can be raised up to the quenching temperature Tq with retaining the surface temperature of the steel material at Acm line temperature or less.
  • the quenching temperature Tq is preferably equal to, or higher than, the temperature at which the core portion of the steel material becomes an austenite single phase.
  • the time of retaining the temperature at the quenching temperature Tq is not particularly limited, and an optimal time is to be selected depending upon composition of the steel material, quenching temperature Tq, characteristic properties required for the steel material, and the like. In general, as the temperature-retaining time is prolonged, the surface carbon concentration of the steel material can be more increased. In order to obtain high-concentration carburized steel excellent in abrasion resistance and surface fatigue strength, the temperature-retaining time at the quenching temperature Tq (i.e., carburization time) is preferably 15 minutes or longer.
  • quenching may immediately be performed substantially without performing carburization at the quenching temperature Tq after the temperature reaches the quenching temperature Tq as long as a sufficient carburization amount is obtained at the point when the temperature reaches the quenching temperature Tq and when soaking of the steel material is sufficient.
  • the quenching step is a step of quenching the steel material after completion of the secondary carburization late step.
  • Quenching is to be performed for transforming the surface carburized layer and the core portion to martensite.
  • the steel material after completion of the secondary carburization late step is to be preferably quenched.
  • the quenching method there are specifically an oil quenching method and a gas quenching method.
  • FIGS. 1A to FIG. 1D are schematic views showing structural changes when performing high-concentration carburization under various conditions. Additionally, phase diagrams are also shown in FIGS. 1A to FIG. 1D .
  • the high-concentration carburization it is performed twice in many case, that is, the primary carburization and the secondary carburization.
  • the surface carbon concentration upon completion of the primary carburization is lower than the Acm line concentration corresponding to the carburization temperature as shown in the phase diagram of FIG. 1A . That is, the surface after the completion of the primary carburization is in a state of austenite single phase. Therefore, when the steel material is cooled to 700° C. or lower from this state at a predetermined cooling rate, the structure of the steel material becomes the state wherein coarse carbides are not generated at the grain boundaries as shown in the left drawing of FIG. 1A .
  • the fine carbides generated during temperature-raising procedure act as nuclei to allow growth of carbides as shown in the right drawing of FIG. 1A .
  • the temperature upon completion of the primary carburization must be higher than the Acm line, and the temperature upon initiation of the secondary carburization must be lower than the Acm line. Since produced steel materials are not uniform in composition between lots, the position of the Acm line varies to some extent between individual steel materials. Hence, in order to surely obtain the structure as shown in FIG. 1A , it is necessary to provide a sufficient temperature difference between the primary carburization temperature and the secondary carburization temperature.
  • the structure of the steel material after completion of the primary carburization is in the state that coarse carbides are not generated at the grain boundaries as shown in the left drawing of FIG. 1B .
  • the secondary carburization temperature exceeds the Acm line, fine carbides having been generated within the grains in the course of raising temperature in the secondary carburization again undergoes solid dissolution as shown in the middle drawing of FIG. 1B .
  • nuclei for allowing carbides to grow disappear within the grains, and hence carbides are preferentially generated at the grain boundaries having smaller formation energy.
  • coarse carbides are generated at the grain boundaries as shown in the right drawing of FIG. 1B .
  • the structure of the steel material after completion of the primary carburization is in the state that coarse carbides are not generated at the grain boundaries as shown in the left drawing of FIG. 1D .
  • the secondary carburization start temperature is lower than the primary carburization temperature by 100° C. or more while raising, after cooling the steel material, the temperature to the secondary carburization start temperature, the surface temperature of the steel material can surely be adjusted to temperature lower than the Acm line. Therefore, at the point where the temperature reaches the secondary carburization start temperature, fine carbides are generated within the grains as shown in the middle drawing of FIG. 1D .
  • the primary carburization In order to prevent precipitation of flake-like, coarse carbides at the grain boundaries, the primary carburization must be performed at temperature higher than the Acm line and the secondary carburization must be performed at temperature lower than the Acm line.
  • the manufacturing method for high-concentration carburized steel of the invention can provide a sufficient temperature difference between after completion of the primary carburization and upon initiation of the secondary carburization, and hence generation of flake-like, coarse carbides can surely be suppressed even when steel materials are not uniform in composition between lots. Also, since it is not necessary to raise the temperature of the primary carburization for providing a sufficient temperature difference, durability of the furnace is not reduced. Further, since carburization is continued, after a predetermined time after the temperature reaches the secondary carburization start temperature, by raising the temperature to the quenching temperature, the carbon concentration of the surface can reach the intended concentration in a short time.
  • Carburization is performed with steel materials having various compositions under various conditions. Additionally, every carburization is performed in two steps of the primary carburization and the second carburization. Also, except for Example 15 and Comparative Example 1, the secondary carburization is performed in two steps of the secondary initial step of retaining the temperature for a predetermined time at a definite level (low temperature) and the secondary carburization late step of raising the temperature to the quenching temperature (high temperature) and retaining at the temperature for a predetermined time. A typical carburization treatment pattern is shown in FIG. 2 .
  • the secondary carburization start temperature is set to 750° C., the temperature is raised up to the quenching temperature of 850° C. over 40 minutes with performing carburization and, after the temperature reaches the quenching temperature, quenching is immediately performed.
  • the surface carbon concentration after completion of the primary carburization is determined by measuring distribution of cross-sectional carbon concentration through EPMA and calculating an average carbon concentration in the region of 10 ⁇ m from the surface. Also, diameter of carbide after completion of the primary carburization and diameter after quenching are measured by photographing using SEM after corroding the cross-section of the sample with picral, with the maximum value of the particle size of carbides existing in 1 mm 2 being taken as “particle size of carbides”. Further, fatigue strength after quenching is measured by the rotating bending fatigue test (according to JIS Z 2274).
  • Comparative Example 2 coarse carbides of larger than 10 ⁇ m are generated after quenching. The reason for this is that the primary carburization is excessive and, at the point of completion of the primary carburization, coarse carbides are already generated.
  • Comparative Example 3 coarse carbides of larger than 6 ⁇ m are generated. This may be attributed to that, since the primary carburization is insufficient and the surface carbon concentration does not reach the eutectoid carbon concentration, fine carbides are not generated within the grains at the point when the temperature reaches the secondary carburization start temperature.
  • Comparative Example 5 coarse carbides of larger than 7 ⁇ m are generated. This may be attributed to that, since the retaining time of retaining at the secondary carburization initial temperature is short, the surface temperature of the steel material exceeds the Acm line when the temperature is raised to the secondary carburization late temperature.
  • the fatigue strength is less than 700 MPa.
  • the fatigue strength is 700 MPa or more. This may be attributed to that, since the primary carburization, secondary carburization initial procedure, and secondary carburization late procedure are performed under proper conditions, fine and spherical carbides are formed in a large amount within the grains without generating flake-like, coarse carbides at the grain boundaries.
  • the manufacturing method for high-concentration carburized steel of the invention can be used as a manufacturing method for mechanical members such as shafts, bearings, gear wheels, piston pins, and cams.

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JP2006299836A JP4971751B2 (ja) 2006-11-06 2006-11-06 高濃度浸炭鋼の製造方法
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PCT/JP2007/070953 WO2008056552A1 (fr) 2006-11-06 2007-10-26 Procédé de fabrication d'acier cémenté à haute concentration

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Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20060130935A1 (en) * 2004-12-10 2006-06-22 Daido Stell Co., Ltd. & Honda Moto Co., Ltd. Carburized component and method of manufacturing the same

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5569252A (en) * 1978-11-20 1980-05-24 Komatsu Ltd Carburizing method for steel
JP2808621B2 (ja) 1988-11-28 1998-10-08 大同特殊鋼株式会社 鋼の浸炭処理方法
JPH06108226A (ja) * 1992-09-30 1994-04-19 Daido Steel Co Ltd 鋼製部品の浸炭熱処理方法
JP3385722B2 (ja) * 1994-06-15 2003-03-10 住友金属工業株式会社 浸炭焼入方法
JP3413975B2 (ja) * 1994-08-08 2003-06-09 日本精工株式会社 耐摩耗性に優れた転がり軸受
JP3894635B2 (ja) * 1997-08-11 2007-03-22 株式会社小松製作所 浸炭部材とその製造方法並びに浸炭処理システム

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20060130935A1 (en) * 2004-12-10 2006-06-22 Daido Stell Co., Ltd. & Honda Moto Co., Ltd. Carburized component and method of manufacturing the same

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102912282A (zh) * 2012-10-24 2013-02-06 哈尔滨东安发动机（集团）有限公司 16Cr3NiWMoVNbE材料的二次渗碳工艺方法
US20160123951A1 (en) * 2013-05-10 2016-05-05 Hitachi, Ltd. Software and Method of Calculation of Carbon Concentration Distribution
US10428414B2 (en) 2013-06-26 2019-10-01 Daido Steel Co., Ltd. Carburized component
EP3088550A4 (en) * 2013-12-27 2017-08-02 Nippon Steel & Sumitomo Metal Corporation Carburized-steel-component production method, and carburized steel component
CN104726819A (zh) * 2015-03-20 2015-06-24 上海人本集团有限公司 渗碳钢的热处理渗碳工艺
CN115287584A (zh) * 2022-08-08 2022-11-04 重庆齿轮箱有限责任公司 一种中合金渗碳钢的渗碳淬火方法

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