WO2004059029A1 - Élément cémenté et trempé et son procédé de fabrication - Google Patents

Élément cémenté et trempé et son procédé de fabrication Download PDF

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Publication number
WO2004059029A1
WO2004059029A1 PCT/JP2003/012309 JP0312309W WO2004059029A1 WO 2004059029 A1 WO2004059029 A1 WO 2004059029A1 JP 0312309 W JP0312309 W JP 0312309W WO 2004059029 A1 WO2004059029 A1 WO 2004059029A1
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WIPO (PCT)
Prior art keywords
carburized
quenching
quenched
quenched member
member according
Prior art date
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PCT/JP2003/012309
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English (en)
Japanese (ja)
Inventor
Takao Taniguchi
Kazumasa Tsukamoto
Koji Oobayashi
Tomoki Hanyuda
Yutaka Kurebayashi
Hideo Kanisawa
Seiji Itoh
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Aisin Aw Co., Ltd.
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Priority claimed from PCT/JP2002/013561 external-priority patent/WO2003056054A1/fr
Application filed by Aisin Aw Co., Ltd. filed Critical Aisin Aw Co., Ltd.
Publication of WO2004059029A1 publication Critical patent/WO2004059029A1/fr

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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
    • 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
    • C23C8/80—After-treatment

Definitions

  • the present invention relates to a carburized and quenched member having excellent fatigue strength and dimensional accuracy, and a method for manufacturing the same.
  • gears which are power transmission parts for automatic transmissions, are often made of carburized and quenched members in order to increase both surface hardness and toughness.
  • Conventional carburized and quenched members are formed into a desired shape using case hardened steel (JIS: SCM420H, SCR422OH, SNCM220), and then formed in a carburized atmosphere. It was common to produce by carburizing gas and then quenching in oil.
  • the carburizing and quenching members are required to reduce costs and improve performance more than ever.
  • One of the issues with carburized and quenched members is to further improve the strength after carburizing and quenching, and to improve dimensional accuracy by suppressing quenching distortion more than ever.
  • the present invention has been made in view of such conventional problems, and an object of the present invention is to provide a carburized and quenched member capable of achieving high strength while sufficiently suppressing quenching distortion, and a method of manufacturing the same. . Disclosure of the invention
  • Fe is contained as a main component, and C is 0.10 to 0.50 weight.
  • a carburized layer is formed by carburizing in an antioxidant atmosphere.
  • a method for producing a carburized and quenched member characterized by performing a quenching treatment under the following conditions.
  • the hardenability J in the above one-end quenching test is obtained by the one-end quenching test method (generally called Jomini one-end quenching test method) specified in JIS: G0561.
  • Value. (At 12.5 mm) is the value of the hardenability J at a position 12.5 mm from the water-cooled end face of the bar specimen for the Jomini 1 ⁇ one-end quenching test. It means that.
  • the quenching quenching rate H is an index proposed by Grossmann et al. That indicates the strength of quenching and is widely used.
  • the C content and the Si After forming a carburized layer by carburizing treatment in a non-oxidizing atmosphere using a specific alloy steel whose J is within the above specified range, the conditions of the monotonic cooling and the specified quenching quenching rate Harden to satisfy both conditions of H.
  • the conditions of the monotonic cooling and the specified quenching quenching rate Harden to satisfy both conditions of H.
  • Si is positively contained in the component, and the content thereof is set to 0.50 to 1.5% by weight.
  • the carburizing treatment is performed in an antioxidant atmosphere.
  • the content of Si is less than 0.5% by weight, there is a problem that the above-mentioned improvement effect is small, and in particular, the effect of preventing grain boundary oxidation during carburizing treatment is reduced.
  • 1.5 weight If the ratio exceeds / 0 , there is a problem that the above-mentioned improvement effect becomes saturated and uniform austenite before quenching is difficult.
  • a more preferable range of the Si content is more than 0.5% by weight ⁇ , 0.70% by weight. / 0 or less.
  • the hardenability J of the above material is 35 to 50 (at 12.5 mm). limit. As a result, an excellent quenching effect can be obtained even when the range of the quenching degree H is limited to the above range.
  • the quenchability J is less than 35, the quenching process after carburizing cannot provide a sufficient quenching effect to the carburized layer and the non-carburized part ( ⁇ part). The desired high strength cannot be achieved. Therefore, more preferably, the hardenability J is set to 38 or more.
  • the hardenability J exceeds 50, there is a problem that the transformation stress increases due to an increase in the microstructure transformation rate inside the non-carburized portion, and quenching strain is likely to occur. .
  • the quenching quenching rate H is limited to 0.01 to 0.08 (cm-i).
  • the quenching degree H is less than 0.01 (cmi)
  • the quenching process after carburizing is similar to the case where the quenchability J is less than 35.
  • a sufficient quenching effect cannot be given to the non-carburized portion (inside), and the desired high strength cannot be achieved.
  • the quenching rate H exceeds 0.08 (c mi)
  • the microstructure transformation rate inside the non-carburized part is the same as when the quenchability J exceeds 50. The rise raises the problem that the transformation stress increases and quenching strain is likely to occur.
  • the above quenching treatment must be performed not only in the above range of quenching rate H but also under the condition of monotonically cooling from point A1 to point Ms as described above.
  • Cooling monotonically means that reheating does not occur during cooling, that is, the material temperature during cooling does not rise. Therefore, when the above condition of monotonic cooling is satisfied, if the material temperature continues to drop, or Even if the cooling stops, this includes the case where the temperature becomes constant and never rises, and then falls again. Also, changes in the cooling rate are, of course, permitted.
  • the cooling condition can be selected so as not to cover the nose region of the S curve shown in the so-called isothermal transformation curve in the carburized portion. As a result, sufficient martensitic transformation can be ensured.
  • a second aspect of the present invention is a carburized and quenched member manufactured by the above manufacturing method, wherein the surface hardness of the carburized layer is 700 to 900 Hv, and the non- A carburized and quenched member characterized in that the internal hardness of the carburized part is 250 to 45 OH v.
  • This carburized and quenched member adopts the above-mentioned excellent manufacturing method and adjusts the component range processing conditions to limit the surface hardness of the carburized layer and the internal hardness of the non-carburized portion to the specific ranges described above. Things.
  • the stress distribution applied to the member obtained by combining the stress acting on the member due to the additional load acting on the member and the stress concentration near the member surface caused by the unevenness of the member shape, holes, etc.
  • static strength tensile strength, bending strength, torsional strength, etc.
  • dynamic strength surface fatigue strength, bending fatigue strength, torsional fatigue strength, etc.
  • the surface hardness of the carburized layer is less than 70 OHv, the strength may not be secured against stress concentration near the member surface. Another problem is that the wear resistance on the outermost surface is insufficient. On the other hand, when the surface hardness exceeds 9 ° OHv, carbides such as cementite may be generated on the surface layer, which may lead to insufficient strength, especially toughness.
  • Figure 1 is an explanatory diagram showing a rotating bending fatigue test piece.
  • Figure 2a is a plan view of the evaluation gear. ..,,
  • Figure 2b is a cross-sectional view of the evaluation gear.
  • the carburizing treatment is preferably performed in a reduced-pressure atmosphere reduced to 1 to 30 hPa.
  • a reduced-pressure atmosphere reduced to 1 to 30 hPa. This makes it possible to easily obtain the antioxidant atmosphere by reducing the pressure, and to sufficiently prevent grain boundary oxidation during carburization. If the value of the decompression in the decompression atmosphere is less than l hPa, there is a problem in that it is excessive for suppressing oxidation, and the equipment for decompression has a high decompression specification, resulting in an increase in cost.
  • the carburizing treatment is performed in an atmosphere containing an inert gas as a main component. Also in this case, the above-described oxidation preventing atmosphere can be easily formed.
  • the inert gas include nitrogen gas and argon gas.
  • the carburizing treatment is performed so that the surface carbon content of the carburized layer is 0.6 to 1.5 wt ° / 0 .
  • the surface carbon concentration of the carburized layer affects the surface hardness of the carburized and quenched material. If the surface carbon content of the carburized layer is less than 0.6% by weight, there is a problem that the surface hardness is insufficient. If it exceeds 1.5% by weight, there is a problem that the hardenability of the matrix is remarkably reduced due to an increased amount of carbide precipitation and the surface hardness is insufficient.
  • the grain boundary oxidation generated from the surface of the above-mentioned material is 3 ⁇ or less. That is, it is preferable to control the above-mentioned grain boundary oxidation to 3 ⁇ m or less from the surface by adjusting the composition of the material, the antioxidant atmosphere during carburization, the heating temperature, the heating time, and the like.
  • the grain boundary strength decreases. Therefore, the strength is lower than that of general carburized and quenched layers (parts), and when grain boundary oxidation occurs deeper than 3 zm, There is a possibility that abrasion resistance may be reduced due to insufficient strength or hardness of the member.
  • the surrounding alloying elements are also incorporated into the grain boundary acid by chemical compound reaction. As a result, the hardenability improving element in the carburized quenched layer around the grain boundary oxide is taken in and consumed by the grain boundary oxide, and a dead zone of the additive is generated around the grain boundary oxide layer. Insufficient hardenability of the charcoal quenched layer itself may cause insufficient hardness and insufficient strength.
  • the material preferably has a surface compressive residual stress of 300 to 80 OMPa. That is, it is preferable that the residual compressive stress on the surface be adjusted to 300 MPa or more by adjusting the component composition of the material, the antioxidant atmosphere during carburization, the heating temperature, the heating time, and the like. As a result, the tensile stress near the surface The working stress can be reduced by the compressive residual stress in the vicinity of the surface, and in particular, the dynamic strength (surface fatigue strength, bending fatigue strength, torsional fatigue strength) can be improved. On the other hand, if the above surface compressive residual stress exceeds 800 MPa, the cooling rate during quenching must be increased beyond the limit in order to increase the amount of martensite. As a result, large quenching distortion occurs, and the dimensional accuracy of the members cannot be secured.
  • the residual surface compressive residual stress can be obtained by quenching the carburized layer to generate martensite and generating a compressive stress field by volume expansion accompanying transformation.
  • a sufficient compressive residual stress field cannot be formed. Therefore, reducing the retained austenite (specifically, to 25% or less) and reducing the troostite structure (specifically, to 10% or less) require such compression residual It works advantageously from the viewpoint of enhancing stress effect.
  • the absorption of volume expansion during martensitic transformation reduces the stress due to plastic deformation of the surrounding residual austenite or troostite structure when the amount of martensite is small. Does not contribute much.
  • the amount of martensite decreases as described above the residual austenite or troostite structure decreases as described above, the density of dislocations introduced by plastic deformation increases, and slip deformation is constrained. Increase rapidly.
  • quenching process it is preferable to perform quenching under the condition of monotonously cooling in the range of the quenching degree H from the temperature in the austenite region to 300 ° C. Good. As a result, a sufficient quenching effect can be obtained. On the other hand, if the quench rate H during cooling from the temperature in the austenitic region to 300 ° C is less than 0.01 (cmi), quenching is insufficient, and the desired quenched structure and characteristics are obtained. Cannot be secured, resulting in insufficient member strength.
  • quenching quenching rate H in the cooling from the temperature in the austenite region to 300 ° C exceeds quenching quench rate H of 0.08 (c mi)
  • quenching quench rate H of 0.08 (c mi) the quenching is excessive and Transformation stress and thermal stress increase, quenching strain increases, and component accuracy may decrease.
  • the quenching treatment is quenching by gas cooling.
  • the above quenching degree H can be relatively easily secured.
  • the gas cooling is performed with an inert gas.
  • an inert gas Preferably, safety during quenching can be ensured.
  • the inert gas is a nitrogen gas.
  • Nitrogen gas is preferably used as the above inert gas in terms of availability, cost, and ease of handling during mass production operations.
  • the residual austenite area ratio of the carburized layer is 25% or less. If the area ratio of retained austenite exceeds 25%, the retained austenite is converted into martensite due to the working process after the carburizing and quenching process, or due to the applied stress and temperature changes during use of the member. Weaving transformation occurs, and distortion is generated by the transformation stress at that time, and there is a possibility that the accuracy of parts may be reduced.
  • the area ratio of retained austenite is more desirably 20% or less.
  • the retained austenite can be forcibly converted to martensite by, for example, shot peening to reduce the area ratio.
  • the area of the troostite structure on the surface layer of the carburized layer can be reduced.
  • the ratio is preferably 10% or less.
  • the above-mentioned troostite is formed in the carburized layer after carburizing and quenching. Since the structure is incompletely quenched and the hardness is low, if the area ratio of the structure exceeds 10%, the strength of the component may be reduced by low-strength troostite.
  • the internal structure of the carburized and quenched member is preferably bainite. More specifically, the area ratio of bainite in the sectional structure is desirably 50% or more. Bainite, unlike martensite, undergoes transformation while iron atoms forming the lattice partially diffuse. Therefore, compared to martensite, the occurrence of distortion due to transformation is small, and the hardness is higher than the pearlite generated when the cooling rate is further reduced, so that the strength of the inner non-carburized portion is appropriately increased. be able to.
  • the inner layer is composed mainly of bainite, by setting the cooling quenching rate H in the range of 0.01 to 0.08 (c mi), it is possible to obtain a structure mainly composed of bainite. It is desirable to select the composition in advance. This makes it possible to obtain parts that have both strength and toughness.
  • the carburized and quenched member is a carburized gear.
  • Gears are parts that require a variety of strict conditions, and the excellent characteristics obtained by the above manufacturing method are very effective.
  • Example 1 the results of an experiment performed to confirm the effects of the present invention will be described.
  • steel steel (steel 11 to 14) having the chemical composition shown in Table 1 was melted in an arc furnace and then hot-rolled into round bars with a diameter of 150 mm and a diameter of 32 mm. 1 o'clock on C After the holding, air-cooled normalizing was performed.
  • Steels 11 and 12 are steel grades having the component compositions newly developed in this example, and steels 13 and 14 are JIS case hardened steels SCM 420 and SN CM 8 15 respectively. It is a steel grade corresponding to
  • the hardenability J was determined by performing a Jomini end quench test based on JIS: GO561.
  • Table 1 shows the results. This property is a property of the material that is not related to the manufacturing method described later.
  • Steel 11 and Steel 12 are alloy steels applicable to the material of the present invention in terms of material and hardenability J.
  • steel 13 has hardenability J and Si content outside the range of the present invention
  • steel 14 has Si content outside the range of the present invention.
  • test spur gear 4 (equivalent round bar diameter 10. ⁇ ) was produced.
  • the test pieces and gears made from the above steels 11, 12, and 14 were subjected to low-pressure carburizing (vacuum carburizing) and gas quenching under the conditions of “Production method 1” shown in Table 2.
  • each test piece made of steel 13 was subjected to gas carburizing and oil quenching under the conditions of “Method 2” shown in Table 3.
  • “Production method 1” has a quenching quenching rate ⁇ of 0.05 (c mi) after carburizing treatment, and satisfies the requirements of the production method of the present invention. .
  • the following tests were performed on the test pieces prepared as described above.
  • the hardness distribution (internal hardness) of the cross section of a round bar specimen with a diameter of 25 mm was examined using a Vickers hardness meter.
  • the surface hardness (surface hardness) of the carburized and quenched material was measured at 0.02 mm from the surface.
  • the area ratio of troostite at the same position was measured by image analysis of a scanning electron micrograph.
  • the maximum oxide layer depth was measured from the surface metallographic structure of the lower layer of the grain boundary acid using an optical microscope.
  • the surface carbon concentration was measured at 50 xm from the surface using an X-ray macro analyzer. Further, the residual austenite area ratio was measured member surface using a C o-kappa alpha rays in X-ray diffraction apparatus.
  • the surface residual stress was measured by the half-width half-point method using an X-ray stress meter using the Fe-line.
  • Step type 11 carburized and quenched material “Steel 11, 12 + Manufacturing method 1” obtained by treating Steel 11 and Steel 12 by Manufacturing method 1 (hereinafter the combination of steel type and manufacturing method is referred to as “Steel type 11”). + Manufacturing method), the hardness at the center is 25 OHv or more. Both the surface layer and the central part; the weave is martensite, and there is no remarkable incompletely quenched structure.
  • gear accuracy and dimensional accuracy of the gears were evaluated as follows.
  • a dedicated precision gear accuracy measuring machine was used to measure the amount of error in each direction of gear pressure and the amount of error in the torsion angle direction on each of the left and right tooth surfaces.
  • the tooth space height was measured over the entire circumference, and the value obtained by subtracting the minimum value from the maximum value was calculated as the tooth groove runout.
  • the carburized layer was formed by carburizing in an antioxidant atmosphere using a specific alloy steel whose C content, Si content, and hardenability J were within the above specified range. Later, in the case of “Steel 11, 12 + Production method 1” quenched under the conditions of the specific quenching and quenching degree H, it is possible to achieve high strength while sufficiently suppressing quenching distortion. Understand.
  • alloy steel has Fe as a main component and C: 0.12-0.22 mass 0 / as an auxiliary component.
  • a 1: 0. 005 ⁇ It should be set so that it contains 0.05 mass%.
  • N of steel types 11 and 12 is 87.6 and 93.4, respectively, and N is larger than 95 for steel types 13 and 14 outside the component range of the present invention. If N exceeds 9.5, the hardness in the rolled state and the hardness in the normalized state of the steel will increase significantly, making it impossible to obtain machinability and cold workability. Therefore, when emphasis is placed on manufacturability, it is necessary to control the composition of the steel so that the composition parameter N is 95 or less.
  • bainite is not formed when the cooling rate is at least 0.1 ° C / sec or less, and the cooling rate is at least 12 ° CZ seconds or more. No ferrite is formed in the region.
  • the range of the above cooling rate can be specified by measuring a continuous cooling transformation diagram (CCT diagram) of steel at various cooling rates.
  • CCT diagram continuous cooling transformation diagram
  • ferrite is no longer generated in the steel composition at a cooling rate of at least 12 ° CZ seconds (hereinafter referred to as the upper limit cooling rate) so that the carburized layer is sufficiently quenched even by gas cooling.
  • bainite should not be formed at a cooling rate of at least 0 • 1 ° C / sec. 0. If bainite is formed even at a cooling rate of 1 ° CZ or less, the inner layer, which is not affected by the carburized layer, is deeply quenched and the strain increases.
  • bainite is not formed at a cooling rate of less than 0.1 ° c / sec, the formation of bainite is sufficiently suppressed in the actual annealing cooling rate range, and the workability of ferrite + pearlite is increased. A rich organization can be obtained. Therefore, in the as-annealed state, that is, in the range where the cooling rate from austenite is equivalent to natural cooling or air cooling, a sufficiently low material hardness can be obtained to improve workability, and machining before carburizing and quenching is performed. It can be done easily.
  • the composition so that the inner layer has a structure mainly composed of bainite by setting the cooling rate to 3 in the range of 0.1 to 10. Particularly, when cooling at 3 ° CZs, It is desirable that the main component be tinite.
  • steels having the chemical compositions shown in Table 6 (steels 21 to 24 and steels 31 to 38) were melted, then slab-formed, and then slab-rolled and bar-rolled to obtain a diameter. A 0-mm round bar was manufactured.
  • test pieces and gears were sorted into three types of manufacturing methods (manufacturing methods 3 to 5).
  • “Production method 3” is characterized by gas carburizing and oil quenching, and heating in a carburizing gas atmosphere for 9 hours at 90 ° C for 1 hour ⁇ diffusion for 1 hour at 850 ° C for 1 hour ⁇ oil quenching at 130 ° C ⁇ Carburizing quenching and tempering are carried out at 80 ° C for 1 hour. In this case, the degree of quenching and quenching H is 0.15 (cm'i).
  • “Production method 4” is characterized by vacuum carburization and gas cooling. Heating at 0 ° C for 5 hours ⁇ Diffusion for 1 hour at 850 ° C-cooling with nitrogen gas ⁇ Carburizing and tempering under tempering conditions at 180 ° C for 1 hour. In this case, the quenching rate H is 0.05 (cm " 1 ).
  • steel grades 31 to 38 have low bending fatigue strength or surface fatigue strength, and parts that are oil-cooled have large variations in accuracy due to quenching strain, and there are many practical problems.
  • Steel grades 31 to 34 have an incompletely quenched structure due to the formation of grain boundary oxidation during gas carburization, and their strength is low due to their low surface hardness. In addition, quenching is more rapid and cooling unevenness is greater due to oil cooling than gas cooling, resulting in greater variation in accuracy due to quenching distortion. ,:.
  • the quenching by oil cooling was too strong for the hardenability of the steel material, and the internal hardness was too high.
  • the difference in the ratio between the surface transformation and the internal transformation was reduced, that is, the difference between the surface hardness and the internal hardness was reduced.
  • the surface compressive residual stress was reduced, and the strength was reduced.
  • oil cooling causes quenching to be more rapid than gas cooling, and cooling unevenness is also large, resulting in large variations in accuracy due to quenching distortion.
  • the surface hardness is high, the internal hardness shows an appropriate value, the strain can be suppressed to a small value, and it is clear that both high strength and low strain can be achieved. .
  • the alloy steel has Fe as the main component, the sub-components, C: 0.1-0.5 mass%, and Si: 0.5-1.0 mass. /. , Mn: 0.3 to 1.0 mass. /. , Cr: 0.1 to 1.0% by mass, P: 0.003 to 0.015% by mass. /. , S: 0.00 5 to 0.03 wt%, A 1:. 0. 0 1 ⁇ 0 06 wt%, N: with containing 0.00 5 to 0.03 mass 0/0, Mo: 0. It is preferable to set so as to contain at least one of 3 to 1.3 mass 0 Ni: 0.1 to 1.0 mass ° / 0 . As a further auxiliary component, V: 0.

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  • Chemical Kinetics & Catalysis (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
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  • Organic Chemistry (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
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Abstract

L'invention concerne un procédé permettant de fabriquer un élément cémenté et trempé qui consiste à utiliser, comme matière première, un acier d'alliage contenant Fe comme composant principal, 0,10 à 0,50 % en poids de C et 0,50 à 1,50 % en poids de Si, ledit élément présentant une trempabilité (J) de 35 à 50 (à 12,5 mm) telle que mesurée au moyen d'un essai de trempage d'extrémité. Ledit procédé consiste à former la matière première en un élément présentant une forme désirée; à soumettre l'élément formé à un traitement de cémentation au carbone dans une atmosphère antioxydante afin de former une couche cémentée; et à soumettre l'élément cémenté à un traitement de trempage dans des conditions dans lesquelles ledit élément est refroidi uniformément à partir de son point de transformation perlite (point A1) à son point de début de transformation martensite, le degré (H) de refroidissement rapide pendant le trempage étant de 0,01 à 0,08 (cm-1). L'invention concerne également un élément cémenté et trempé fabriqué au moyen de ce procédé. On peut améliorer la résistance de l'élément cémenté et trempé par suppression acceptable de ses contraintes de trempage et sans augmentation de ses coûts de production
PCT/JP2003/012309 2002-12-25 2003-09-26 Élément cémenté et trempé et son procédé de fabrication WO2004059029A1 (fr)

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JPPCT/JP02/13561 2002-12-25

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2869246A1 (fr) * 2004-04-27 2005-10-28 Renault V I Sa Procede de fabrication de pieces d'un couple conique
CN102011055A (zh) * 2010-12-10 2011-04-13 燕山大学 硬贝氏体轴承制造方法
CN108570640A (zh) * 2018-05-29 2018-09-25 沈阳飞机工业（集团）有限公司 一种柱销局部渗碳方法

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JPH11310824A (ja) * 1998-04-30 1999-11-09 Aisin Aw Co Ltd 浸炭焼き入れ鋼部材及びその製造方法
US6258179B1 (en) * 1997-08-11 2001-07-10 Komatsu Ltd. Carburized parts, method for producing same and carburizing system
WO2003056054A1 (fr) * 2001-12-25 2003-07-10 Aisin Aw Co., Ltd. Element carbure et trempe et son procede de production

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Publication number Priority date Publication date Assignee Title
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FR2869246A1 (fr) * 2004-04-27 2005-10-28 Renault V I Sa Procede de fabrication de pieces d'un couple conique
CN102011055A (zh) * 2010-12-10 2011-04-13 燕山大学 硬贝氏体轴承制造方法
CN108570640A (zh) * 2018-05-29 2018-09-25 沈阳飞机工业（集团）有限公司 一种柱销局部渗碳方法

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