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WO2011013559A1 - Procédé de traitement thermique combiné et élément d'acier trempé - Google Patents

Procédé de traitement thermique combiné et élément d'acier trempé Download PDF

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WO2011013559A1
WO2011013559A1 PCT/JP2010/062269 JP2010062269W WO2011013559A1 WO 2011013559 A1 WO2011013559 A1 WO 2011013559A1 JP 2010062269 W JP2010062269 W JP 2010062269W WO 2011013559 A1 WO2011013559 A1 WO 2011013559A1
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compound layer
nitrogen compound
nitrogen
layer
steel
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PCT/JP2010/062269
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English (en)
Japanese (ja)
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剣吾 深沢
佳孝 三阪
一博 川嵜
芳宏 池田
正昭 別府
知義 小西
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高周波熱錬株式会社
日本パーカライジング株式会社
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Publication of WO2011013559A1 publication Critical patent/WO2011013559A1/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
    • 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
    • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
    • C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
    • 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
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/30—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for crankshafts; for camshafts
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/32—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for gear wheels, worm wheels, or the like
    • 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
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding 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
    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the present invention relates to a composite heat treatment method and a hardened steel member for producing a hardened steel member used as a machine structural part having excellent mechanical strength such as surface pressure strength, wear resistance, and bending fatigue strength.
  • steel and cast iron mechanical structural parts such as shafts, gears, pistons, shafts, and cams are nitrided to improve mechanical strength such as surface pressure strength, wear resistance, and bending fatigue strength.
  • Surface hardening treatment such as treatment, soft nitriding treatment, carburizing quenching, induction hardening is applied.
  • a nitrogen compound layer formed on the surface of a steel substrate by nitriding or soft nitriding is known to have excellent slidability, resistance to wear, and high seizure resistance (hereinafter referred to as this). This will be referred to as effect I by the nitrogen compound layer.)
  • This nitrogen compound layer is formed by diffusing and penetrating nitrogen into the steel substrate by performing nitriding treatment or soft nitriding treatment on the surface of the steel substrate.
  • the steel materials that contain diffused nitrogen have a fine martensite structure that is obtained after quenching in a state containing diffused nitrogen, which increases the hardness and improves hardenability.
  • the formation of a nitrogen diffusion layer by nitriding treatment or soft nitriding treatment can also be used as a nitrogen diffusion penetrating treatment that increases the hardness of the steel material (hereinafter referred to as effect II by the nitrogen compound layer). ).
  • This effect II is not due to the action of the nitrogen compound layer itself, but due to the action of diffused nitrogen in the steel material immediately below the nitrogen compound layer generated when the nitrogen compound layer is formed.
  • Formation of a nitrogen diffusion layer by nitriding or soft nitriding causes an increase in surface pressure strength and fatigue strength in addition to an increase in steel hardness.
  • the martensitic structure containing diffusion nitrogen obtained by quenching is due to the fact that it has resistance to temper softening and resistance to crack initiation / growth in addition to the above-mentioned increase in hardness and improvement in hardenability. It is known to have high surface pressure strength and high fatigue strength.
  • the quenching temperature needs to be at least the temperature Ac3 transformation point at which an austenite structure is formed, and is usually selected from a temperature range of 750 to 1050 ° C.
  • the nitrogen compound layer formed at a nitriding temperature of 570 ° C. is a combination of iron and nitrogen, and is oxidized and decomposed when reheated to 650 ° C. or higher in the air atmosphere. Then, it is released as nitrogen gas and the nitrogen compound layer disappears. This has been reported for a long time (Non-Patent Document 1).
  • the combined heat treatment technology by nitriding and quenching usually uses only the effect II caused by the nitrogen diffusion layer obtained in the surface layer portion of the steel material by nitriding treatment, and nitrogen formed in the surface layer portion of the steel material by nitriding treatment
  • the characteristic (effect I) of excellent slidability, high wear strength, and high seizure resistance resulting from the fact that the compound layer has diffused nitrogen is not utilized. That is, the nitrogen compound layer does not stop disappearing during quenching, which is a subsequent process of nitriding.
  • the composite heat treatment described in Patent Documents 1 to 5 can be mentioned.
  • Patent Document 6 discloses a composite heat treatment method in which a nitriding treatment is performed at a temperature of 600 ° C. or higher to form a nitrogen compound layer having a thickness of 5 ⁇ m or less, followed by induction hardening to obtain a quenched member having a nitrogen compound layer having a thickness of 2 ⁇ m or less. ing.
  • the reason why the nitriding conditions are set to a high temperature of 600 ° C. or higher in this composite heat treatment method is that a higher concentration of nitrogen diffusion can be expected toward the deeper side of the steel material at higher temperatures.
  • a nitrogen compound layer obtained at a nitriding temperature exceeding 600 ° C. is a nitrogen compound layer having a low hardness and having no effect I. That is, this composite heat treatment method is only expected to have the effect II by the nitrogen compound layer, and the remaining nitrogen compound layer of 2 ⁇ m or less may be omitted.
  • the nitrogen compound layer is not oxidized or decomposed during induction hardening.
  • a hardened steel material is manufactured by coating with a protective film having a thickness of 1 to 3 mm comprising a gas nitriding / ion nitriding inhibitor, carburizing inhibitor and antioxidant containing silicon oxide as a component, followed by quenching.
  • This method solves the problem of damage and disappearance of the nitride layer caused by high-temperature heating by induction hardening of the nitride layer formed on the surface of the steel material as it is, and is a method of combining effects I and II.
  • the hardened steel member disclosed in Patent Document 8 is formed by forming a hard nitride layer on the surface of a steel material by nitriding, and then converting the hard nitride layer into Ti, Zr, Hf, V, Nb, Ta, Cr, It is manufactured by coating with an inorganic nitrogen compound layer (protective film) containing at least one metal oxide selected from the group consisting of W, Mo and Al, followed by quenching.
  • an inorganic nitrogen compound layer protecting film
  • a protective film is formed on the hard nitride layer so that the hard nitride layer is not oxidized or decomposed during induction hardening.
  • the steel member is provided with a deep hardening depth as well as a nitrogen compound layer. This hardened steel member can have both effects I and II.
  • nitriding or soft nitriding is inferior in surface pressure strength, fatigue strength, and the like as compared with carburizing and induction hardening.
  • the nitrogen compound layer may peel off from the steel substrate. If the hard nitrogen compound layer is peeled off, the debris can be fatally damaged in gear parts. For this reason, it has been widely believed that the nitrogen compound layer has a rather adverse effect in the fatigue test at a high surface pressure exceeding 2 GPa.
  • the nitrogen compound layer is formed after induction hardening. It has been considered necessary to peel off.
  • the nitrogen compound layer is formed as long as the base of the nitrogen compound layer is hard and the hard part is deep. It was confirmed by a fatigue test, a gear single unit test, and the like that it could not be peeled even at a high surface pressure exceeding 2 GPa, and it was confirmed that the nitrogen compound layer was not an essential damage factor for gear parts and the like.
  • the present inventors do not lie in the fact that the nitrogen compound layer is peeled off because the surface pressure strength and fatigue strength of the nitrogen compound layer itself are inferior to those of carburizing and induction hardening, but support the nitrogen compound layer. It was found that the effective hardened layer depth of the substrate was shallow. That is, the cause of the peeling of the outermost nitrogen compound layer formed by nitriding is that the effective hardened layer depth immediately below the layer is insufficient.
  • the present invention is a composite heat treatment method for producing a hardened steel member that combines nitriding treatment and induction hardening, and is used for protection against oxidation on a nitrogen compound layer formed on the surface of a steel substrate. Without covering the film, a good nitrogen compound layer remains after induction hardening, and has the above effects I and II, and the effective hardened layer of the steel substrate covered with the nitrogen compound layer has high surface pressure strength, high Combined heat treatment method for manufacturing hardened steel members with fatigue strength and high mechanical strength in terms of surface pressure strength, wear resistance and bending fatigue strength, and mechanical structural parts such as shafts, gears, pistons, shafts, cams, etc. It is an object of the present invention to provide a suitable hardened steel member.
  • the present invention includes a step of forming a nitrogen compound layer on the surface of a steel substrate by nitriding and diffusing nitrogen into a surface layer portion of the steel substrate covered with the nitrogen compound layer, and quenching.
  • the atmosphere is an ammonia gas atmosphere, an inert gas atmosphere, a reducing gas atmosphere, a combination gas atmosphere thereof, a low-oxidation atmosphere, or a high-frequency quenching in a vacuum, leaving an unoxidized nitrogen compound layer of 1 ⁇ m or more and a nitrogen compound.
  • the oxidation of the nitrogen compound layer is suppressed during induction hardening without covering the nitrogen compound layer formed by nitriding the surface of the steel base material with an anti-oxidation protective film, and nitrogen is added.
  • the compound layer an unoxidized region remains in the depth direction by 1 ⁇ m or more. Therefore, the presence of this nitrogen compound layer makes it possible to produce a hardened steel member that is excellent in slidability, resistant to wear, and has high seizure resistance (effect I by the nitrogen compound layer).
  • the formation process of the nitrogen compound layer is also used as a nitrogen diffusion pretreatment for forming a nitrogen diffusion layer for improving the hardenability in the surface layer portion of the steel substrate (effect II by the nitrogen compound layer).
  • the hardenability is improved, and the effective hardened layer depth of 200 ⁇ m or more including the diffused nitrogen on the surface side and the fine martensite structure is increased immediately after the nitrogen compound layer by induction hardening performed thereafter. It can be provided in the surface layer portion of the substrate.
  • the effective hardened layer depth and the fatigue strength correlate, and the fatigue strength increases as the effective hardened layer depth increases.
  • the nitrogen-containing martensite structure obtained by quenching has high surface pressure strength and high resistance due to its resistance to temper softening and crack initiation / growth in addition to increased hardness and improved hardenability. Has fatigue strength.
  • the peel strength of the nitrogen compound layer with respect to the steel substrate can be kept large, and therefore it has excellent slidability, wear resistance, and seizure.
  • the effect of the nitrogen compound layer having a high resistance characteristic can be fully utilized.
  • a thick effective hardened layer depth can be obtained under the layer by induction hardening while keeping the nitrogen compound layer healthy. Combined with the fact that it is not martensite but fine martensite containing nitrogen, it can withstand high surface pressure fatigue tests.
  • a combined heat treatment combining nitriding treatment and induction hardening can leave a nitrogen compound layer formed on the surface of a steel substrate in a good state that is not oxidized even after induction hardening in an excellent state.
  • tissue can be deeply formed with 200 micrometers or more in the outermost layer part of the surface layer part of the steel base material which is a foundation
  • This martensite structure includes a fine martensite structure containing diffusion nitrogen of 50 ⁇ m or more.
  • the peel strength of the nitrogen compound layer with respect to the steel substrate can be ensured to be large compared with the case where the effective hardened layer depth can be obtained only in the conventional composite heat treatment, and the nitrogen compound layer on the outermost surface. It was confirmed that the good slidability can be fully utilized, and no adverse effect is exerted even in a fatigue test under a high surface pressure exceeding 2 GPa.
  • the present invention provides a surface layer portion in which a nitrogen compound layer having a hardness of HV550 or more and not oxidized remains 1 ⁇ m or more on the surface of the steel substrate and is covered with the nitrogen compound layer of the steel substrate.
  • a fine martensite structure containing nitrogen is included, and the effective hardened layer depth exceeding HV550 is 200 ⁇ m or more in terms of the distance from the surface of the steel substrate.
  • a nitrogen compound layer that is not oxidized after induction hardening remains 1 ⁇ m or more. Therefore, the presence of the nitrogen compound layer in the quenched steel member is excellent in slidability, resistance to wear, and seizure resistance. Have high characteristics (effect I by nitrogen compound layer I).
  • the nitrogen compound layer is supported by a thick effective hardened layer including a martensite structure as a base, and the surface side portion of the hardened region is not a simple martensite structure but a fine martensite structure containing nitrogen,
  • a thick effective hardened layer including a martensite structure as a base
  • the surface side portion of the hardened region is not a simple martensite structure but a fine martensite structure containing nitrogen
  • it has high tempering softening resistance, high surface pressure strength and high fatigue strength due to resistance to crack initiation and growth, and fatigue performed under high surface pressure exceeding 2 GPa
  • the effect I of the nitrogen compound layer can be fully utilized as compared with the conventional product in which the peel strength of the nitrogen compound layer with respect to the steel substrate is shallow in the effective hardened layer.
  • the nitrogen compound layer formed on the surface of the steel substrate is coated with an anti-oxidation protective film. Therefore, it can be protected from oxidation during induction hardening, and a good nitrogen compound layer remains 1 ⁇ m or more after induction hardening, and the mechanical strength, sliding resistance and anti-resistance based on the characteristics of the nitrogen compound layer remain.
  • the formation of a nitrogen compound layer increases the hardness of the surface portion of the steel substrate and improves hardenability (Effect II), as well as resistance to temper softening and cracking.
  • a hardened steel member having high surface pressure strength and high fatigue strength resulting from resistance to generation / growth can be produced.
  • the peel strength of the nitrogen compound layer with respect to the steel substrate is kept large, and thus it has excellent slidability, wear resistance, and seizure resistance. Therefore, it is possible to provide a hardened steel member that can fully utilize the characteristics of the nitrogen compound layer that have high properties.
  • a hardened steel member suitable as a mechanical structural part such as a shaft, a gear, a piston, a shaft, and a cam can be provided.
  • FIG. It is a typical manufacturing process figure of the hardened steel member concerning the embodiment of the present invention. It is a figure of the optical microscope photograph image which shows the cross-sectional state after quenching using the test material by Example 1.
  • FIG. It is a graph which shows the cross-sectional hardness distribution of the cross-sectional hardness measurement result after quenching using the test material by Example 2.
  • FIG. It is a figure which shows the optical microscope photographic image after quenching using the test material by Example 3, and a SEM micrograph image. It is a figure of the optical microscope photograph image and SEM microscope photograph image which concern on the comparative example 2.
  • the hardened steel member according to this embodiment is a hardened steel member manufactured by a combined heat treatment method combining nitriding treatment and induction hardening, as shown in FIGS. 1 (a) to 1 (c). In this hardened steel member, as shown in FIG.
  • a nitrogen compound layer 2 having a hardness of HV550 or higher that is not oxidized remains on the surface 1a of the steel base 1 at 1 ⁇ m or more, and the nitrogen compound layer
  • the effective hardened layer 1c exceeding HV550 having a distance of 200 ⁇ m or more from the surface is formed on the surface layer portion 1d of the steel substrate 1 covered with 2, and the fine martens containing diffusion nitrogen of 50 ⁇ m or more from the surface It is a highly cured layer that greatly exceeds HV550 including the site structure.
  • the method for manufacturing the quenched steel member is based on a combined heat treatment method combining nitriding treatment and induction hardening, as shown in FIGS. 1 (a) to 1 (c).
  • the steel substrate 1 shown in FIG. 1 (a) is placed in a nitriding facility and heated to 350 ° C. to 600 ° C. to nitride the surface 1a of the steel substrate 1.
  • the nitriding treatment is any one of salt bath soft nitriding treatment, gas nitriding treatment, gas soft nitriding treatment or plasma nitriding treatment.
  • a nitrogen diffusion layer 1b having a distance of 50 ⁇ m or more from the surface is formed on the surface layer portion 1d of the steel substrate 1, and the surface 1a of the steel substrate 1 has a hardness.
  • a nitrogen compound layer 2 of HV550 or higher is formed.
  • the steel substrate 1 on which the nitrogen compound layer 2 is formed is placed in an induction hardening facility and induction hardened.
  • the quenching atmosphere is an ammonia gas atmosphere, an inert gas atmosphere, a reducing gas atmosphere or a combination gas atmosphere thereof, or a low oxidation atmosphere or a vacuum.
  • the surface layer portion 1d of the steel substrate 1 can be heated to 750 ° C. to 860 ° C. instantaneously with respect to the surface layer portion 1d of the specific steel substrate by using the high frequency coil 1 to 2 seconds at the longest. Heat to 750 ° C. to 860 ° C. per second, immediately quench, and finish induction hardening.
  • the nitrogen compound layer 1b that is not oxidized after quenching remains 1 ⁇ m or more, and the surface is formed on the surface layer portion 1d of the steel substrate 1 immediately below the nitrogen compound layer 2.
  • the steel substrate 1 to which the present embodiment is applied is not particularly limited, and examples thereof include carbon steel, low alloy steel, medium alloy steel, high alloy steel, cast iron and the like. Preferred materials from the viewpoint of cost are carbon steel, low alloy steel, and the like.
  • carbon steel for machine structure (S20C to S58C) is suitable as carbon steel, and nickel chrome steel (SNC236 to SNC836), nickel chrome molybdenum steel (SNCM220 to SNCM815), chrome as low alloy steel.
  • Molybdenum steel materials (SCM415 to SCM445, SCM822), chromium steel materials (SCr415 to SCr445), manganese steel materials for mechanical structures (SMn420 to SMn443), manganese chromium steel materials (SMC420 to SMC443) and the like are suitable. These steel materials do not necessarily need to use a tempered steel material (H material) that guarantees hardenability by tempering, and may use a tempered steel material that remains in an untempered ferrite-pearlite structure. .
  • H material tempered steel material
  • the nitrogen compound layer 2 on the surface 1a of the steel substrate 1 diffuses and infiltrates active nitrogen from the surface 1a of the steel substrate 1 and is hard and stable on the surface 1a of the steel substrate 1. Obtained by nitriding to form nitride.
  • nitride mainly containing Fe as a base material component and containing Ti, Zr, Mo, W, Cr, Mn, Al, Ni, C, B, Si and the like. It is preferable that it is a layer.
  • the above effect I can be achieved, such as salt bath nitriding treatment such as tuftride (registered trademark) treatment, isonite (registered trademark) treatment, pulsonite (registered trademark) treatment, gas soft nitriding treatment, plasma nitriding treatment, etc.
  • salt bath nitriding treatment such as tuftride (registered trademark) treatment, isonite (registered trademark) treatment, pulsonite (registered trademark) treatment, gas soft nitriding treatment, plasma nitriding treatment, etc.
  • Any nitriding method can be used as long as it has a method in which a nitrogen-diffused region is formed in the nitrogen compound layer and the steel substrate portion immediately below.
  • the heating temperature of the nitriding treatment for forming the nitrogen compound layer having the above effect I is preferably 350 ° C. to 600 ° C.
  • a nitrogen compound layer necessary for exhibiting good performance cannot be sufficiently formed on the surface of the steel substrate, and nitriding is performed at a temperature exceeding 600 ° C.
  • the higher the temperature the higher the concentration of nitrogen diffusion toward the deeper side of the steel material can be expected.
  • the hardness of the resulting nitrogen compound layer is low, and the nitrogen compound layer has no effect I due to the nitrogen compound layer.
  • the heating temperature on the upper limit side is preferably 580 ° C. or lower, more preferably 570 ° C. or lower, from the viewpoint of obtaining high hardness.
  • a nitrogen diffusion layer 1b having a distance of 50 ⁇ m or more from the surface is formed on the surface layer portion 1d of the steel substrate 1. Can be generated.
  • this portion can be a highly hardened layer that greatly exceeds the Vickers hardness HV550 after induction hardening, and can have sufficient high surface pressure strength and high fatigue strength. .
  • the peel strength of the nitrogen compound layer to the steel substrate is kept large, so that it is excellent in slidability, wear resistance, and seizure resistance. It is possible to make full use of the characteristics of the nitrogen compound layer, which has high properties.
  • the nitrogen compound layer 2 can be formed on the surface layer portion 1d of the steel substrate 1.
  • the thickness of the nitrogen compound layer 2 obtained by nitriding before induction hardening is not particularly limited, but the nitrogen compound layer 2 when the nitrogen diffusion layer 1b of 50 ⁇ m or more is formed is formed with a thickness of 1 ⁇ m or more.
  • the nitriding process may be terminated.
  • the thickness of the nitrogen compound layer 2 is preferably 2 ⁇ m to 20 ⁇ m, and more preferably 3 ⁇ m to 15 ⁇ m. If processing time is lengthened, it can form in thickness of 30 micrometers.
  • the nitrogen compound layer When performing induction hardening in a quenching atmosphere such as an ammonia gas atmosphere other than a low oxidation atmosphere, the oxidation of the surface of the nitrogen compound layer can be completely suppressed.
  • the nitrogen compound layer may be formed to a thickness of 1 ⁇ m or more.
  • the surface portion of the nitrogen compound layer is oxidized, so the thickness of the nitrogen compound layer is determined in consideration of the oxidation depth, and the oxidized portion is scraped off. In this step, a nitrogen compound layer having a thickness of at least 1 ⁇ m is left.
  • induction hardening is performed in a gas atmosphere, a low-oxidation atmosphere, or in a vacuum that can prevent oxidation of the nitrogen compound layer.
  • examples of the gas atmosphere that can prevent oxidation of the nitrogen compound layer include an ammonia gas atmosphere, an inert gas atmosphere, a reducing gas atmosphere, or a combination thereof. These gas atmospheres are preferable to the low oxidation atmosphere.
  • a vacuum is preferable because it takes equipment and running time to form an ultra-high vacuum.
  • examples of the reducing gas atmosphere include petroleum gases such as hydrogen, propane, and butane, modified gases thereof, alcohols, esters, and ketones.
  • an inert gas neutral gas, such as nitrogen and argon, or those combinations are mentioned.
  • the high-frequency heating is performed by a high-frequency heating coil that reaches the heating temperature set to 750 ° C. to 860 ° C. on the surface layer of the object to be processed (steel base material). After reaching a temperature of 750 ° C. to 860 ° C., a fine martensite structure containing nitrogen can be obtained by immediately cooling with a coolant.
  • the heating temperature during induction hardening is set to 750 ° C. to 860 ° C.
  • the nitrogen diffusion layer 1b becomes a fine martensite structure due to rapid cooling, and no excessive residual austenite exists, and good induction hardening can be performed.
  • a more preferable heating temperature is 770 ° C. to 840 ° C.
  • a further preferable heating temperature is 780 ° C. to 830 ° C.
  • the heating temperature is lower than 750 ° C., nitrogen is contained and it is easy to quench, but at this temperature, the steel base material is not sufficiently austenitized, so that quenching becomes insufficient.
  • a heating temperature exceeding 860 ° C. is not preferable because excessive retained austenite is easily generated in the martensitic structure immediately below the nitrogen compound layer.
  • the high frequency heating is preferably performed for about 1 second by a high frequency heating coil that reaches a heating temperature set at 750 ° C. to 860 ° C. It is preferable that the limit is about 4 seconds at the longest.
  • a multistage temperature raising method including preheating can be appropriately performed.
  • a tempering treatment may be performed under appropriate conditions in the same manner as a normal quenching technique.
  • the nitrogen compound layer 2 is heated by heat transfer from the surface 1a of the steel substrate 1 within a short quenching time, and the inner surface is high and the surface has a low temperature gradient. Therefore, the disappearance of nitrogen on the surface of the nitrogen compound layer 2 due to oxidation or decomposition is sufficiently suppressed.
  • the surface of the steel substrate is provided with a nitrogen compound layer having HV550 or more in terms of Vickers hardness and having a thickness of 1 ⁇ m to 30 ⁇ m, and immediately below the nitrogen compound layer of the steel substrate, A martensitic structure having an effective hardened layer depth of 200 ⁇ m or more (depth of layer having HV550 or more in terms of Vickers hardness) at a distance from the surface can be obtained, and 50 ⁇ m of the outermost layer portion of the effective hardened layer depth.
  • a highly hard layer including not only a normal martensite structure but also a fine martensite structure containing diffusion nitrogen and having a Vickers hardness greatly exceeding HV550 can be obtained.
  • the effective hardened layer of HV550 or higher has a hardness distribution that is not uniform in the depth direction and gradually decreases from the surface to the inside.
  • the hardened layer containing a fine martensite structure containing nitrogen greatly exceeds the hardness of HV550.
  • a hardness of HV630 or higher can be obtained.
  • the effective hardened layer depth of the martensite structure including the fine martensite structure containing nitrogen is 400 ⁇ m or more depending on the condition settings such as the depth of the fine martensite structure containing diffusion nitrogen, the induction hardening temperature, and the type of the steel substrate. Furthermore, it is possible to obtain a steel material having a hardness distribution so that it is 600 ⁇ m or more.
  • the nitrogen compound layer remains after high-frequency heating, but the nitrogen compound layer does not necessarily remain 100% with respect to the state of the nitrogen compound layer before high-frequency heating, and the minimum film thickness is 1 ⁇ m or more. It is sufficient that the compound layer thickness remains. More preferably, it is 2 ⁇ m or more, and more preferably 3 ⁇ m or more.
  • the surface layer portion that has been oxidized or decomposed may be removed as necessary, and even if the thickness of the nitrogen compound layer is reduced thereby, the minimum film thickness may be 1 ⁇ m or more.
  • the surface layer portion of the nitrogen compound layer that has been oxidized or decomposed is brittle and has low hardness, so that it can be easily removed.
  • lapping treatment emery paper polishing, buffing, shot blasting, shot peening can be used.
  • the heating temperature for quenching by high-frequency heating is 750 to 860 ° C.
  • the quenching temperature is sufficiently lower than the induction quenching and carburizing quenching usually performed at a temperature exceeding 900 ° C.
  • the steel material to which the present embodiment is applied does not need to use a tempered steel for the effect of improving the hardenability of the effect II by nitrogen, and has a ferrite-pearlite structure that is a non-tempered steel. Sufficient mechanical strength can be obtained even with steel. Further, although alloy steel tends to have a slightly higher surface hardness, a sufficiently deep effective hardened layer depth can be obtained even with inexpensive carbon steel due to the effect II of nitrogen.
  • a carbon steel for mechanical structure such as S45C is a heat treatment material having a hardness profile with sufficient hardness and sufficient depth.
  • S45C does not need to be a tempered material, and even if the heat treatment of this embodiment is applied to a steel member with a non-tempered ferrite-pearlite structure, it becomes a heat-treated machine part having sufficient mechanical strength. obtain.
  • the application of this embodiment improves the mechanical strength of parts, reduces the cutting process, and switches to inexpensive materials, thereby reducing the size and weight of the entire machine parts by reducing the size of the parts, and nitriding and induction hardening. It is possible to reduce the actual cost by surplus to compensate for the cost increase due to the combined processing.
  • the hardened steel member according to the present invention is suitable for use as a mechanical structural component having excellent mechanical strength such as surface pressure strength, wear resistance, bending fatigue strength, etc., particularly in a high load / high surface pressure region. Suitable for what is used.
  • the hardened steel member according to the present invention is not particularly limited with respect to the shape and part type of the steel member. Examples of hardened steel members include shafts, gears, pistons, shafts, cams, and the like, which are suitable for transmission-related parts and powertrain parts for automobiles and construction equipment.
  • a high frequency is applied to the surface of the steel substrate using an induction hardening apparatus in an ammonia gas atmosphere, the surface is heated to 860 ° C. for 0.8 seconds, and immediately cooled (water cooled) without taking a holding time. ) And quenched.
  • the hardened steel member was cut with a microcutter, embedded in a resin, and subjected to cross-sectional observation with a metal microscope. As a result, a micrograph image shown in FIG. 2 was obtained. From this micrograph image, it was confirmed that iron nitride having a thickness of 7 ⁇ m that was not oxidized remained on the surface of the steel substrate. Moreover, cross-sectional hardness measurement was performed using a micro Vickers hardness tester using this embedded sample. As a result, the Vickers hardness measured at a depth of 0.1 mm from the surface of the steel substrate was 816 Hv. Moreover, when the depth of Vickers hardness 550Hv used as an effective hardened layer was measured, it was 1.25 mm from the surface.
  • a high frequency is applied to the surface of the steel substrate using an induction hardening apparatus in an argon gas atmosphere, the surface is heated to 820 ° C. over 1.0 second, and immediately cooled without taking a holding time ( It was quenched with water.
  • the quenched steel member was cut with a microcutter, embedded in resin, and cross-section was observed with a metal microscope. As a result, it was confirmed that iron nitride with a thickness of 10 ⁇ m that was not oxidized remained on the surface of the steel substrate.
  • FIG. 3 shows the cross-sectional hardness distribution of the measurement results.
  • the Vickers hardness at a depth of 0.1 mm from the surface of the steel material substrate was 720 Hv
  • the depth of the Vickers hardness 550 Hv serving as an effective hardened layer was 0.74 mm from the surface.
  • the hardened steel member was cut with a microcutter, embedded in resin, and observed with a metal microscope to obtain a micrograph image shown in FIG. From this micrograph image, it was confirmed that the iron nitride remaining in the non-oxidized state on the surface of the steel substrate was less than 1 ⁇ m in thickness. Moreover, cross-sectional hardness measurement was performed using a micro Vickers hardness tester using this embedded sample. As a result, the Vickers hardness measured at a depth of 0.1 mm from the surface of the steel substrate was Hv815. Moreover, when the depth of Hv550 or more used as an effective hardened layer was measured, it was 1.28 mm from the surface.
  • Table 1 shows a list of numerical values of the measurement results of Example 1, Example 2, and Comparative Example 1.
  • Example 1 and Example 2 As shown in FIG. 2, the nitrogen compound layer on the surface remained without significant damage even after induction hardening.
  • the non-oxidized nitrogen compound layer remains with a sufficient thickness larger than 1 ⁇ m, so that effects I and II can be obtained, and the effective hardened layer has a thickness of 200 ⁇ m or more. Since there are 0.1 mm or more highly hardened layers that greatly exceed Hv550, the nitrogen compound layer has high surface pressure strength and high fatigue strength.
  • Comparative Example 1 it was observed from FIG. 4 that the entire nitrogen compound layer was oxidized. Therefore, since the hardened steel member of Comparative Example 1 does not have a nitrogen compound layer, the effect I cannot be obtained, and only the effect II can be obtained.
  • FIG. 5 shows an optical microscope photograph image obtained by cutting a quenched specimen obtained when the heating temperature during quenching is 830 ° C. with a microcutter, embedding in a resin, and observing a cross section with a metal microscope. And SEM micrograph images.
  • Table 2 shows a table comparing the chemical composition of the SCM440 specimen of Example 3 with the chemical composition of the SCM440 JIS standard.

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Abstract

L'invention concerne un élément d'acier trempé obtenu par formation, au moyen d'un traitement de nitruration, d'une couche (2) de composition d'azote sur la surface d'un substrat d'acier (1), diffusion d'azote sur une partie superficielle (1d) du substrat d'acier (1) recouvert de la couche (2) de composition d'azote, et grâce au trempage par induction dans une atmosphère de gaz ammoniac, sous vide ou dans une atmosphère à faible teneur en oxygène, conservation de la couche (2) de composition d'azote non on oxydée après le trempage sur une épaisseur supérieure ou égale à 1 μm, et sur une partie superficielle (1d) du substrat d'acier (1), attribution à une couche durcie comprenant une microstructure de martensite contenant de l'azote d'une profondeur de couche durcie efficace supérieure ou égale à 200 μm. Ainsi, même si on applique sur la couche (2) de composition d'azote de la surface d'un substrat d'acier (1) une pression de contact supérieure à 2GPa, on obtient un élément d'acier trempé très résistant au décollement par rapport à l'acier de la couche (2) de composition d'azote, et suffisamment efficace grâce à la couche (2) de composition d'azote dont la capacité de glissement est excellente, et laquelle est résistante à l'abrasion et présente une grande résistance à la cuisson.
PCT/JP2010/062269 2009-07-31 2010-07-21 Procédé de traitement thermique combiné et élément d'acier trempé WO2011013559A1 (fr)

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WO2016078924A1 (fr) * 2014-11-19 2016-05-26 Thyssenkrupp Steel Europe Ag Procédé de formage à chaud ou à basse température d'une pièce et installation de production pour le formage à chaud ou à basse température d'une pièce
US9617632B2 (en) 2012-01-20 2017-04-11 Swagelok Company Concurrent flow of activating gas in low temperature carburization
WO2018006887A1 (fr) * 2016-07-07 2018-01-11 Bonatrans Group A.S. Essieu pour véhicules ferroviaires
WO2021230384A1 (fr) * 2020-05-15 2021-11-18 Ｊｆｅスチール株式会社 Composant en acier
CN115612972A (zh) * 2022-09-27 2023-01-17 南京丰东热处理工程有限公司 钢表面层厚可控的含氮马氏体复合改性层及其工艺方法
KR102808718B1 (ko) * 2020-05-15 2025-05-16 제이에프이 스틸 가부시키가이샤 강 및 강 부품

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US9212416B2 (en) 2009-08-07 2015-12-15 Swagelok Company Low temperature carburization under soft vacuum
US10156006B2 (en) 2009-08-07 2018-12-18 Swagelok Company Low temperature carburization under soft vacuum
US10934611B2 (en) 2009-08-07 2021-03-02 Swagelok Company Low temperature carburization under soft vacuum
US9617632B2 (en) 2012-01-20 2017-04-11 Swagelok Company Concurrent flow of activating gas in low temperature carburization
US10246766B2 (en) 2012-01-20 2019-04-02 Swagelok Company Concurrent flow of activating gas in low temperature carburization
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WO2016078924A1 (fr) * 2014-11-19 2016-05-26 Thyssenkrupp Steel Europe Ag Procédé de formage à chaud ou à basse température d'une pièce et installation de production pour le formage à chaud ou à basse température d'une pièce
WO2018006887A1 (fr) * 2016-07-07 2018-01-11 Bonatrans Group A.S. Essieu pour véhicules ferroviaires
CN109476177A (zh) * 2016-07-07 2019-03-15 博纳特兰集团合股公司 用于轨道车辆的轴
CZ308546B6 (cs) * 2016-07-07 2020-11-18 Bonatrans Group A.S. Náprava pro kolejová vozidla
WO2021230384A1 (fr) * 2020-05-15 2021-11-18 Ｊｆｅスチール株式会社 Composant en acier
JPWO2021230384A1 (fr) * 2020-05-15 2021-11-18
WO2021230383A1 (fr) * 2020-05-15 2021-11-18 Ｊｆｅスチール株式会社 Acier et composant d'acier
JPWO2021230383A1 (fr) * 2020-05-15 2021-11-18
CN115605629A (zh) * 2020-05-15 2023-01-13 杰富意钢铁株式会社（Jp） 钢和钢部件
CN115605628A (zh) * 2020-05-15 2023-01-13 杰富意钢铁株式会社（Jp） 钢部件
JP7306580B2 (ja) 2020-05-15 2023-07-11 Ｊｆｅスチール株式会社 鋼および鋼部品
JP7306581B2 (ja) 2020-05-15 2023-07-11 Ｊｆｅスチール株式会社 鋼部品
KR102808718B1 (ko) * 2020-05-15 2025-05-16 제이에프이 스틸 가부시키가이샤 강 및 강 부품
CN115612972A (zh) * 2022-09-27 2023-01-17 南京丰东热处理工程有限公司 钢表面层厚可控的含氮马氏体复合改性层及其工艺方法

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