WO2008056552A1 - Procédé de fabrication d'acier cémenté à haute concentration - Google Patents

Procédé de fabrication d'acier cémenté à haute concentration Download PDF

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Publication number
WO2008056552A1
WO2008056552A1 PCT/JP2007/070953 JP2007070953W WO2008056552A1 WO 2008056552 A1 WO2008056552 A1 WO 2008056552A1 JP 2007070953 W JP2007070953 W JP 2007070953W WO 2008056552 A1 WO2008056552 A1 WO 2008056552A1
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Prior art keywords
temperature
carburizing
carburization
steel
primary
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PCT/JP2007/070953
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English (en)
Japanese (ja)
Inventor
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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Priority to EP07830687A priority Critical patent/EP2085493A4/fr
Priority to CN2007800413430A priority patent/CN101535522B/zh
Priority to US12/447,914 priority patent/US20100126632A1/en
Publication of WO2008056552A1 publication Critical patent/WO2008056552A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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 method for producing high-concentration carburized steel, and more particularly to a method for producing high-concentration carburized steel capable of precipitating a large amount of fine and spherical carbides on the surface by carburizing treatment. .
  • Carburization refers to a process in which steel is heated in a carburizing atmosphere to increase the carbon concentration on the surface.
  • Carburizing is generally applied to low-carbon steel and is used after being carburized.
  • Such carburized and hardened materials are called case hardened steel or carburized steel, and since the surface is hard and the inside is soft, it is awarded for machine parts such as shafts, bearings, gears, piston pins and cams. Has been.
  • high-concentration carburizing the process of increasing the carbon concentration near the surface of the material and precipitating carbides is called “high-concentration carburizing”.
  • the material obtained by high-concentration carburization has hard carbides dispersed in the structure, so it has higher wear resistance and surface fatigue strength than conventional materials obtained by eutectoid carburization! / There is a characteristic.
  • the characteristics of the high-concentration carburized material are strongly influenced by the dispersion form of the carbides. Therefore, in order to obtain high strength, it is necessary to disperse the carbides in fine and spherical shapes (non-patent document 1). reference). In particular, coarse carbides precipitated at grain boundaries cause a decrease in strength.
  • Patent Document 1 a machine structural component manufactured from steel containing C: 0.05 to 0.45% is disclosed.
  • a method for carburizing steel which has a surface C concentration of 1.7% or more, and the carburized layer has a substantially spherical carbide shape and has excellent wear resistance and pitting resistance.
  • the document includes:
  • Patent Document 2 describes that steel parts having a surface carbon concentration of 0.8% or more by carburizing treatment are not less than 0.1 l ° C / s ec up to a temperature of 300 ° C or less after this carburizing treatment.
  • the steel part is then heated to a temperature range 50 ° C higher and 150 ° C lower than the Acl transformation temperature of the steel. After that, the temperature is maintained at the same temperature, and further heated to a temperature at which the core is austenite single phase or two phases of austenite and ferrite and the ferrite area ratio is 30% or less at a heating temperature of 10 ° C / sec or less.
  • a carburizing heat treatment method for steel parts is disclosed in which quenching is performed directly after quenching or after lowering the temperature to a predetermined quenching temperature.
  • This document states that fine carbides can be grown by keeping carburized steel parts in a temperature range that is 50 ° C higher and 150 ° C lower than the Acl transformation temperature of the steel.
  • Non-Patent Document 1 Tetsuya Shimomura, Toshiyuki Morita, Koichiro Inoue Electric Steelmaking, Vol. 77 (2006), p. 11
  • Patent Literature 1 Japanese Patent Gazette: 2808621
  • Patent Document 2 Japanese Published Patent Publication: Hei 6-108226
  • the temperature of the primary carburizing is increased to increase the temperature difference between the primary carburizing and the secondary carburizing, the life of the furnace is reduced.
  • the case-hardened steel is usually used as it is without being finished, but heating at a higher temperature than necessary causes the deformation of the material to increase.
  • the temperature of the primary carburizing steel If the temperature of the secondary carburization is lowered at the same time as lowering the carbon, the carbon diffusion rate during the secondary carburization will decrease. For this reason, it takes a long time to precipitate the necessary amount of carbide, and the working efficiency is lowered.
  • the problem to be solved by the present invention is to provide a method for producing high-concentration carburized steel capable of dispersing a large amount of fine and spherical carbides without reducing the life of the furnace.
  • Another problem to be solved by the present invention is to provide a method for producing high-concentration carburized steel that does not cause significant deformation after carburizing treatment.
  • Another problem to be solved by the present invention is to provide a method for producing high-concentration carburized steel that can disperse a large amount of fine and spherical carbides without reducing the working efficiency.
  • Another problem to be solved by the present invention is to provide a method for producing a high-concentration carburized steel in which flakes and coarse carbides do not precipitate at grain boundaries and the structure is highly reproducible.
  • a method for producing a high-concentration carburized steel according to the present invention includes:
  • the steel material is raised to the secondary carburization start temperature T2s, and the secondary carburization temperature T2 is V, and the steel material is carburized in the initial stage of secondary carburization (however, the Acl point (° C) ⁇ T2s ( ° C) ⁇ primary carburizing temperature Tl-100 ° C ⁇ A cm line temperature (° C) equivalent to the surface carbon concentration of the steel immediately after the start of secondary carburizing, T2s ⁇ T2 ⁇ surface carbon concentration of the steel The corresponding Acm line temperature (° C)),
  • the secondary carburizing initial process in which the secondary carburizing is performed at a secondary carburizing temperature T2 lower than the quenching temperature Tq.
  • the carburizing is performed at the quenching temperature Tq, it is divided into the second stage of secondary carburizing, and even if the primary carburizing temperature T1 is relatively low, the temperature difference between the primary carburizing temperature T1 and the secondary carburizing temperature T2 The ability to take S Therefore, it is possible to disperse a large amount of fine and spherical carbides without reducing the life of the furnace or causing large deformation after carburizing.
  • FIG. 1 A schematic diagram and a state diagram of a structure change when high-concentration carburization is performed under various conditions.
  • FIG. 2 is a diagram showing a typical carburizing pattern used in the examples.
  • the steel material to which the method according to the present invention is applied contains the following alloy elements, with the balance being Fe and inevitable impurities.
  • the types of alloy elements, their component ranges, and the reasons for their limitations are as follows.
  • the C content is preferably 0.15 mass% or more.
  • the amount of c is excessive, the hardness of the material is increased and the manufacturability (particularly machinability) is lowered. Accordingly, the C content is preferably 0.30 mass% or less.
  • the Si content is preferably 0.40 mass% or more.
  • the Si content 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 Cr content is preferably 1.25 ma SS % or more.
  • the Cr amount is preferably 2.00 mass% or less.
  • the manufacturing method of the high concentration carburized steel according to the present invention includes a primary carburizing step, a cooling step, a secondary carburizing initial step, a secondary carburizing late step, and a quenching step.
  • the primary carburizing step is a step of carburizing a steel material having the above composition so that the surface carbon concentration C is Ceu ⁇ C ⁇ C (Acm) at the primary carburizing temperature Tl (° C). It is.
  • the primary carburizing temperature T1 may be at least 100 ° C higher than the secondary carburizing start temperature T2s described later. In general, the higher the primary carburizing temperature T1, the shorter the time required for carburizing to a predetermined carbon concentration. Specifically, the primary carburizing temperature T1 is preferably 900 ° C or higher.
  • the primary carburizing temperature T1 is specifically preferably 1100 ° C or less, more preferably 1000 ° C or less.
  • Carburization is performed so that the surface carbon concentration C of the steel material is Ceu ⁇ C ⁇ C (Acm).
  • surface carbon concentration refers to the average carbon concentration within a region of 10 ⁇ from the surface.
  • “Ceu” refers to the eutectoid carbon concentration of steel containing Si, Mn, and Cr in the above-mentioned range. In any of the above steel materials, the eutectoid carbon concentration is 0.5 ma SS % or more.
  • C (Acm) means the carbon concentration corresponding to the Acm line of the steel material containing Si, Mn and Cr in the above-mentioned range at the primary carburizing temperature T1. Carburizing until C ⁇ C (Acm) means that the primary carburizing is performed at a temperature where the surface temperature of the steel material is higher than the Acm line (ie, the temperature at which the surface becomes a single ⁇ phase).
  • C (Acm) is about 1.25 to 4 mass%.
  • the carburizing method for performing the primary carburizing is not particularly limited, and it is possible to use various methods.
  • gas carburizing and vacuum carburizing are suitable as carburizing methods because they are easy to handle and have a short processing time.
  • the carbon concentration C on the surface can be kept within the above range by optimizing the carburizing conditions.
  • gas carburizing is performed by heating a steel material in a carburizing gas atmosphere.
  • the carburization amount can be controlled by the carbon potential of the carburizing atmosphere.
  • Carbon potential is the surface equilibrium carbon concentration of pure iron that is in equilibrium with the atmosphere. Depends on the CO / CO ratio and the amount of HO in the atmosphere. In general, the higher the carbon potential and / or the higher the primary carburizing temperature T1, the higher the surface carbon concentration.
  • vacuum carburizing involves depressurizing the inside of a furnace containing steel materials to about 1.3 Pa, heating it to the carburizing temperature, and introducing hydrocarbon gases such as methane and propane into the furnace. I do.
  • the carburization amount can be controlled by the introduction time of the hydrocarbon gas.
  • the carbon concentration near the surface may become too high. In such a case, the supply of hydrocarbon gas is stopped after carburizing, and diffusion treatment is performed to maintain that state. Is common.
  • the cooling step is a step of cooling the steel material to a temperature of 700 ° C or lower at a cooling rate of 1 ° C / min or higher after the completion of the primary carburizing step.
  • the steel After the completion of primary carburization, the steel is cooled to a temperature of 700 ° C or less.
  • the reason for cooling to a temperature of 700 ° C or lower is to precipitate fine carbides in the grains when reheating the secondary carburization. In this case, if the cooling rate is too slow, it is not preferable because flakes and coarse carbides precipitate at the grain boundaries during cooling. Coarse carbides generated during cooling do not disappear even in the process described later, and cause a reduction in the strength of the steel material. Therefore, the cooling rate is preferably 1 ° C / min or more. The faster the cooling rate, the better.
  • the secondary carburizing initial step is a step of raising the temperature of the cooled steel material to the secondary carburizing start temperature T2s and carburizing the steel material at the secondary carburizing temperature T2.
  • second carburization start temperature T2s refers to a temperature that satisfies the following equation (1).
  • the temperature difference between the secondary carburizing start temperature T2s and the primary carburizing temperature T1 is preferably 100 ° C or higher. If the temperature difference between the two is less than 100 ° C, flaky and coarse carbides may form at the grain boundaries. The larger the temperature difference between the two, the better.
  • the secondary carburization start temperature T2s needs to be not less than the Acl point and not more than the Acm line temperature corresponding to the surface carbon concentration of the steel immediately after the start of the secondary carburization. This is because the surface temperature of the steel is between the Acl point and the Acm line (that is, the temperature at which the surface becomes the ⁇ + Fe C phase). ) Means to start secondary carburization.
  • the "secondary carburizing temperature T2" is a temperature that satisfies the following condition (2)!
  • Secondary carburizing temperature T2 may or may not be the same as the secondary carburizing start temperature T2s Higher temperature.
  • the holding time at the secondary carburizing temperature T2 is that the surface temperature of the steel material becomes equal to the Acm line temperature when the temperature is raised to the quenching temperature Tq described later. If it ’s over V or time, V. In general, the longer the holding time at the secondary carburizing temperature T2, the higher the carbon concentration on the surface, and accordingly the surface Acm line temperature also rises, so the steel surface temperature remains below the Acm line. Can perform carburizing power. In order to ensure that the surface temperature of the steel material is below the Acm line when the temperature is raised to the quenching temperature Tq, which will be described later, the holding time at the secondary carburizing temperature T2 is preferably 15 minutes or more.
  • the secondary carburizing temperature T2 when the secondary carburizing temperature T2 is higher than the secondary carburizing start temperature T2s, the secondary carburizing temperature T2 may be increased stepwise from the secondary carburizing start temperature T2s or continuously. May be raised.
  • “Stair-like” means that after holding at a constant temperature for a predetermined time, the temperature is raised by a predetermined temperature range, and then holding at that temperature for a predetermined time is repeated. Even when the temperature is raised stepwise, carburization can be performed while keeping the surface temperature of the steel material below the Acm line if the temperature rise and the holding time at the holding temperature are optimized.
  • Continuous refers to increasing the temperature at a predetermined rate of temperature increase. Even when the temperature is raised continuously, carburization can be performed while keeping the surface temperature of the steel material below the Acm line by optimizing the heating rate.
  • the second stage of secondary carburization is a process in which the steel material is continuously heated to the quenching temperature Tq (° C) after the initial stage of the second carburizing and further carburized at the quenching temperature Tq.
  • Tq ⁇ Acm line temperature (° C) corresponding to the surface carbon concentration of the steel.
  • the second stage of the second carburizing process is performed in a short period of time, in which carburization is performed at a higher temperature than simply raising the temperature of the steel material to the quenching temperature Tq, so that flakes and coarse carbides precipitate at the grain boundaries. It is also a process for making the carbon concentration of the target carbon concentration. Therefore, the quenching temperature Tq must be below the Acm line temperature corresponding to the surface carbon concentration of the steel material.
  • the quenching temperature Tq In general, the lower the quenching temperature Tq, the more flaky and coarse carbides are produced at the grain boundaries during holding. However, if the quenching temperature Tq is too low, quenching of the core becomes insufficient as the carbon diffusion rate decreases. Therefore, it is preferable that the quenching temperature Tq is equal to or higher than the temperature at which the core of the steel material becomes an austenite single phase.
  • the holding time at the quenching temperature Tq is not particularly limited, and an optimum time is selected according to the composition of the steel material, the quenching temperature Tq, the characteristics required for the steel material, and the like. In general, the longer the holding time, the higher the surface carbon concentration of the steel material. In order to obtain a high-concentration carburized steel with excellent wear resistance and surface fatigue strength, the holding time at the quenching temperature Tq (that is, the carburizing time) is preferably 15 minutes or more.
  • the quenching step is a step of quenching the steel material after the end of the second stage carburizing process.
  • Quenching is performed in order to transform the carburized layer and the core of the surface into martensite. For this purpose, it is preferable to rapidly cool the steel material after the end of the second stage carburizing process.
  • quenching methods include oil quenching and gas quenching.
  • Fig. 1 ⁇ to Fig. 1 (d) show schematic diagrams of the structural changes when carburized at high concentration under various conditions. Figures 1 (a) to 1 (d) also show state diagrams.
  • High-concentration carburizing is often performed in two cases: primary carburizing and secondary carburizing.
  • conventional high-concentration carburizing which is performed in two stages, the carbon concentration on the surface at the end of primary carburization is lower than the Acm line concentration corresponding to the carburizing temperature, as shown in the phase diagram of Fig. 1 (a). It is concentration.
  • the surface after the primary carburization is in an austenite single phase state. Therefore, when cooled from this state to 700 ° C or less at a predetermined cooling rate, the steel structure becomes as shown in Fig. 1 (a). As shown in the left figure, no coarse carbide is generated at the grain boundaries.
  • the temperature at the end of primary carburization is higher than the Acm line.
  • the temperature at the start of secondary carburization must be lower than the Acm line.
  • the manufactured steel has component variations between lots, and the position of the Acm line varies slightly for each steel.
  • the steel structure after the completion of the primary carburizing is As shown in the left figure of Fig. 1 (b), no coarse carbides are formed at the grain boundaries.
  • the secondary carburization start temperature exceeds the Acm line, as shown in the middle figure of Fig. 1 (b)
  • the grain size is increased during the secondary carburizing process.
  • the fine carbides generated inside are re-dissolved. Since there are no nuclei for the growth of carbides in the grains, carbides are preferentially produced at grain boundaries with lower formation energy. As a result, coarse carbides are formed at the grain boundaries as shown in the right figure of Fig. 1 (b).
  • the primary carburization is terminated with the primary carburization temperature being equal to or lower than that of the conventional case, as shown in the left diagram of FIG. 1 (d), the structure of the steel material after the completion of the primary carburization. Is in a state where coarse carbides are not generated at the grain boundaries.
  • the secondary carburization start temperature is set to 100 ° C or more lower than the primary carburization temperature, the surface temperature of the steel material will be lower than the Acm line. It can be taken with certainty. Therefore, when the secondary carburization start temperature is reached, fine carbides are generated in the grains as shown in the middle figure of Fig. 1 (d).
  • the manufacturing method of the high-concentration carburized steel according to the present invention can take a sufficient temperature difference between the end of the primary carburization and the start of the secondary carburization, so that there is lot-to-lot variation in the steel materials. However, it is possible to reliably suppress the formation of flakes and coarse carbides. In addition, since it is not necessary to raise the primary carburizing temperature in order to obtain a sufficient temperature difference, the durability of the furnace is not reduced. In addition, 2 After reaching the next carburizing start temperature, the carburization is continued by raising the quenching temperature after a predetermined time, so that the surface carbon concentration can reach the target concentration in a short time.
  • the steel materials having various compositions were carburized under various conditions. Carburization was performed in two stages: primary carburization and secondary carburization. In addition, except for Example 15 and Comparative Example 1, secondary carburization is the initial stage of secondary carburization that is held for a certain period of time at a constant temperature (low temperature), and the temperature is raised to the quenching temperature (high temperature) and held for a certain period of time. This was divided into two stages, the second stage of secondary carburizing. Figure 2 shows a typical carburizing pattern.
  • Carburization is performed in the primary carburization, the initial stage of secondary carburization, and the late stage of secondary carburization.
  • Example 15 the secondary carburization start temperature was set to 750 ° C, the temperature was raised over 40 minutes while carburizing until the quenching temperature reached 850 ° C, and after quenching temperature was reached, quenching was performed immediately. went.
  • the initial stage of the second carburizing process in Comparative Example 2 is an operation of flowing carburizing gas for 3% of the total carburizing time, an operation of carburizing by flowing a carburizing gas, and an operation of evacuating and diffusing for 22% of the total carburizing time. was repeated a total of 4 times.
  • the carburizing gas was poured for a time corresponding to 1% of the total carburizing time, and carburizing was performed for 24% of the total carburizing time. , Repeated a total of 4 times.
  • the surface carbon concentration after the end of primary carburization was calculated by measuring the carbon concentration distribution in the cross section with EPMA and calculating the average carbon concentration in the region of 10 ⁇ from the surface.
  • Carbide particle size after the completion of primary carburization and after quenching can be photographed using SEM after the sample cross section is corroded with picral.
  • the maximum value of the particle size of carbide existing in lmm2 was defined as “carbide particle size”.
  • the fatigue strength after quenching was measured by a rotating bending fatigue test (based on JIS Z 2274).
  • Table 1 shows the components of various steel materials, carburizing conditions, and test results.
  • Comparative Example 1 coarse carbides exceeding 10 in were produced after quenching. This is because the initial stage of the second carburization was omitted and the second stage of the second carburization was immediately performed at 885 ° C, so that the fine carbides generated during the secondary carburization temperature rise were dissolved again. Conceivable.
  • Comparative Example 2 coarse carbides exceeding 10 in were formed after quenching. This is because the primary carburization was excessive and coarse carbide had already been formed at the end of the primary carburization.
  • the method for producing high-concentration carburized steel according to the present invention can be used as a method for producing machine parts such as a shaft, a bearing, a gear piston pin, and a cam.

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Abstract

Cette invention porte sur un procédé de fabrication d'un acier cémenté à haute concentration qui permet de réaliser une dispersion d'un nombre important de carbures fins et sphériques sans provoquer de baisse de durée de service d'un four, de déformation de produits d'acier ni d'abaissement de rendement de traitement. Le procédé de fabrication comprend (i) une étape de cémentation primaire afin de cémenter un produit d'acier ayant une composition prédéterminée à une température de cémentation primaire (Ti) (°C) jusqu'à ce que la concentration de carbone de surface (C) atteigne une concentration de carbone prédéterminée, (ii) une étape de refroidissement pour, après l'achèvement de l'étape de cémentation primaire, refroidir le produit d'acier à une vitesse de refroidissement non inférieure à 1°C/min jusqu'au point Ar1 ou moins, (iii) une étape initiale de cémentation secondaire de façon à élever la température du produit d'acier à une température de départ de cémentation secondaire (T2S) qui est au moins de 100 % au-dessous de la température de cémentation primaire (T1), et cémenter le produit d'acier à une température de cémentation secondaire (T2), (iv) une étape ultérieure de cémentation secondaire pour, après l'achèvement de l'étape initiale de cémentation secondaire, élever la température du produit d'acier à une température de durcissement par trempe (Tq) puis cémenter le produit d'acier à la température de durcissement par trempe (Tq), et (v) une étape de durcissement par trempe pour, après l'achèvement de l'étape ultérieure de cémentation secondaire, durcir par trempe le produit d'acier.
PCT/JP2007/070953 2006-11-06 2007-10-26 Procédé de fabrication d'acier cémenté à haute concentration Ceased WO2008056552A1 (fr)

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EP07830687A EP2085493A4 (fr) 2006-11-06 2007-10-26 Procédé de fabrication d'acier cémenté à haute concentration
CN2007800413430A CN101535522B (zh) 2006-11-06 2007-10-26 高浓度渗碳钢的制造方法
US12/447,914 US20100126632A1 (en) 2006-11-06 2007-10-26 Manufacturing method for high-concentration carburized steel

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JP2006-299836 2006-11-06
JP2006299836A JP4971751B2 (ja) 2006-11-06 2006-11-06 高濃度浸炭鋼の製造方法

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Cited By (3)

* Cited by examiner, † Cited by third party
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JP2016156037A (ja) * 2015-02-23 2016-09-01 大同特殊鋼株式会社 高濃度浸炭鋼の製造方法
CN110923411A (zh) * 2019-12-11 2020-03-27 洛阳北方易初摩托车有限公司 一种箱式多用炉渗碳淬火组织细化工艺方法
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Families Citing this family (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011093070A1 (fr) * 2010-01-27 2011-08-04 Ｊｆｅスチール株式会社 Acier cémenté et matériau carburisé
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WO2014034150A1 (fr) * 2012-09-03 2014-03-06 新日鐵住金株式会社 Composant cémenté
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CN117385314B (zh) * 2023-09-20 2025-09-30 中国航发哈尔滨轴承有限公司 一种G13Cr4Mo4Ni4V钢套圈双重渗碳工艺

Citations (5)

* 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
JPH06108226A (ja) 1992-09-30 1994-04-19 Daido Steel Co Ltd 鋼製部品の浸炭熱処理方法
JPH0849057A (ja) * 1994-08-08 1996-02-20 Nippon Seiko Kk 耐摩耗性に優れた転がり軸受
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
JPH11117059A (ja) * 1997-08-11 1999-04-27 Komatsu Ltd 浸炭部材とその製造方法並びに浸炭処理システム

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3385722B2 (ja) * 1994-06-15 2003-03-10 住友金属工業株式会社 浸炭焼入方法
JP4188307B2 (ja) * 2004-12-10 2008-11-26 大同特殊鋼株式会社 浸炭部品及びその製造方法

Patent Citations (5)

* 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
JPH0849057A (ja) * 1994-08-08 1996-02-20 Nippon Seiko Kk 耐摩耗性に優れた転がり軸受
JPH11117059A (ja) * 1997-08-11 1999-04-27 Komatsu Ltd 浸炭部材とその製造方法並びに浸炭処理システム

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
See also references of EP2085493A4 *
TETSUYA SHIMOMURA; TOSHIYUKI MORITA; KOICHIRO INOUE, DENKI-SEIKO (ELECTRIC FURNACE STEEL), vol. 77, 2006, pages 11

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2016156037A (ja) * 2015-02-23 2016-09-01 大同特殊鋼株式会社 高濃度浸炭鋼の製造方法
CN110923411A (zh) * 2019-12-11 2020-03-27 洛阳北方易初摩托车有限公司 一种箱式多用炉渗碳淬火组织细化工艺方法
CN110923411B (zh) * 2019-12-11 2021-07-30 洛阳北方易初摩托车有限公司 一种箱式多用炉渗碳淬火组织细化工艺方法
CN111826604A (zh) * 2020-07-15 2020-10-27 湖南南方宇航高精传动有限公司 一种在同一零件上不同部位进行差深渗碳的方法
CN111826604B (zh) * 2020-07-15 2022-03-01 湖南南方宇航高精传动有限公司 一种在同一零件上不同部位进行差深渗碳的方法

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US20100126632A1 (en) 2010-05-27
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