EP2530178B1 - Einsatzgehärteter stahl und aufgekohltes material - Google Patents

Einsatzgehärteter stahl und aufgekohltes material Download PDF

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EP2530178B1
EP2530178B1 EP11736785.4A EP11736785A EP2530178B1 EP 2530178 B1 EP2530178 B1 EP 2530178B1 EP 11736785 A EP11736785 A EP 11736785A EP 2530178 B1 EP2530178 B1 EP 2530178B1
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mass
steel
carburization
less
carburized
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EP2530178A4 (de
EP2530178A1 (de
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Katsuyuki Ichimiya
Kazukuni Hase
Hideto Kimura
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JFE Steel Corp
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JFE Steel Corp
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    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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

Definitions

  • the present invention relates to a case hardening steel and a carburized steel material having high fatigue strength, each of which is excellent in cold forgeability, has high fatigue strength after carburization, and suitably serves as a material for mechanical structures in the fields of construction machinery and automobiles.
  • a material of a member to be produced by cold forming of a steel bar e.g. a material of a member of an automobile, is required to have good cold forgeability.
  • steel has been practiced to subject steel to spheroidizing heat treatment to spheroidize carbide in the steel to improve cold forgeability thereof.
  • component composition of steel to decrease content of Si, which significantly affects deformation resistance of the steel.
  • steel in which hardenability-improving properties of boron is effectively utilized.
  • JP-B 3551573 proposes carburized steel for gear, in which contents of alloy elements other than boron can be reduced as much as hardenability of the carburized steel improves due to addition of boron, whereby hardness of the steel can be lowered from the normalizing process to make it possible to remarkably improve gear cutting properties of the steel, as compared with conventional steel.
  • JP-B 3764586 proposes a case hardening steel which ensures good cold formability thereof by combining compositional advantageous effects of reliably improving hardenability by addition of boron and reducing contents of Si and Mn as solute-strengthening elements with a advantageous effect caused by specific production conditions.
  • JP 2006 299383 A and JP 2008 179849 A relate to a steel sheet that undergo a carburizing treatment.
  • gears of increasing smaller sizes are required for gears used in automobiles or the like as vehicle weight is increasingly reduced for better energy saving and also these gears have to bear increasingly higher load exerted thereon as the engine output is increasingly made higher.
  • Durability of a gear is primarily determined by degrees of gear tooth root fracture caused by bending fatigue and pitting fatigue fracture of gear tooth surface. It is known that reducing an incompletely quench-hardened layer appearing at a surface layer during carburization and making prior austenite grains fine are effective in terms of enhancing strength against bending fatigue of a gear tooth root.
  • JP-B 3063399 proposes a carburizing steel having improved fatigue strength and toughness by setting diameter of prior austenite grains to be in the range of 7 ⁇ m or less. Further, JP-B 4056709 proposes finely dispersing carbides in a carburized layer of a steel surface.
  • the present invention has been developed in view of the situation described above and an object thereof is to provide a case hardening steel and a carburized steel material using the case hardening steel, which exhibit excellent cold forgeability respectively, as well as satisfactory high fatigue strength after being carburized.
  • FIG. 1 shows relationships between contents of Al, B and Ti in steel and the maximum particle size of carbide in a surface layer of a super-carburized layer of a case hardening steel. It is understood from FIG. 1 that specifically controlling contents of Al and B and suppressing addition of Ti are critically important in terms of suppressing generation of coarse carbide and finely dispersing carbide.
  • FIG. 1 also shows the results of pitting fatigue strength measurement conducted for some of the steel examples each having the aforementioned super-carburized layer. It is understood from these results that significantly high pitting fatigue strength of steel can be obtained by suppressing generation of coarse carbide.
  • the experiments, of which results are shown in FIG. 1 were conducted by: preparing steel material examples each containing as a base material a steel having the basic composition of 0.2 mass % C, 0.1 mass % Si, 0.6 mass % Mn, 1.5 mass % Cr, 0.02 mass % Nb, with Al and B of specific contents changed between the examples, and the balance as iron and incidental impurities; subjecting these steel material examples to treatments described below; and evaluating the maximum particle diameter ( ⁇ m) of carbide and pitting fatigue strength (MPa) for each steel material example.
  • each of the steel material samples having "super-carburized layers” was prepared by: forming a corresponding steel material into a round bar (25 mm ⁇ ); subjecting the round bar to carburization at relatively high carbon concentration (carbon potential: 2%) at 950°C for 5 hours; cooling the bar to 600°C; heating the bar to 850°C and retaining the bar at the temperature for 30 minutes; and subjecting the bar to oil quenching at 60°C and then tempering treatment at 170°C for 2 hours.
  • the steel material sample thus treated was cut and a cut section thereof was then analyzed by: etching the cut section with picral solution; observing an area ranging from a steel surface to 30 ⁇ m depth (observed area:_6000 ⁇ m 2 ) by using a scan-type electron microscope; and determining the maximum particle diameter of carbide through image analysis.
  • a roller pitting fatigue test was carried out by: collecting a roller pitting fatigue test piece from the round bar; subjecting the roller pitting fatigue test piece thus collected to the aforementioned respective treatments ranging from the carburization at relatively high carbon concentration to the tempering treatment, to obtain a sample; and subjecting the sample to the protocol of a roller pitting fatigue test under the conditions of slip rate: 40% and oil temperature: 80°C, to evaluate 10 7 -cycle strength (the critical strength at which pitting occurs at a surface of the test piece) of the sample.
  • each of the steel material samples having "normally carburized layers” was prepared as a roller pitting fatigue test sample by forming a corresponding steel material into a round bar (25 mm ⁇ ) and collecting a roller pitting fatigue test piece from the round bar.
  • the roller pitting fatigue test piece thus collected was subjected to carburization at carbon concentration of 1.1 mass % at 930°C for 7 hours, oil quenching at 60°C and tempering treatment at 170°C for 2 hours.
  • a roller pitting fatigue test was then carried out by using the roller pitting fatigue test piece thus treated, under the conditions of slip rate: 40% and oil temperature: 80°C, to evaluate 10 7 -cycle strength (the critical strength at which pitting occurs at a surface of the test piece) of the sample.
  • the present invention provides a case-hardening steel having the features defined in claim 1. Further, it is provided a carburized steel material obtained by subjecting the case-hardening steel The carburized steel materials are defined in claims 2 and 3.
  • FIG. 1 is a graph showing how contents of Al, B and Ti affect a state of carbide precipitation.
  • Carbon content in steel needs to be at least 0.10 mass % in order to enhance hardness at the center portion thereof by quenching after carburizing heat treatment.
  • carbon content in steel exceeding 0.35 mass % decreases toughness of the core portion of the steel. Accordingly, carbon content in steel is to be in the range of 0.10 mass % to 0.35 mass % and preferably 0.3 mass % or less.
  • Silicon is required as a deoxidizing agent and need be added to steel by at least 0.01 mass %.
  • silicon is an element which is preferentially oxidized at a carburized surface layer of steel to facilitate oxidization of grain boundaries of the steel. Further, silicon hardens ferrite through solid solution strengthening, thereby increasing deformation resistance of steel and deteriorating cold forgeability of the steel.
  • the upper limit of Si content is to be 0.50 mass % and preferably 0.35 mass %.
  • the lower limit of Si content is preferably 0.03 mass %.
  • Manganese is an element which effectively improves hardenability and need be added to steel by at least 0.40 mass %. However, manganese tends to trigger oxidization of grain boundary and too high content thereof in steel increases retained austenite and lowers surface hardness of the steel. Accordingly, the upper limit of Mn content is 1.50 mass % and preferably 1.40 mass %. The lower limit of Mn content is preferably 0.60 mass %.
  • Phosphorus tends to exist in a segregated manner at crystal grain boundaries and deteriorate toughness of steel. Accordingly, the lower content of phosphorus in steel is the better, although presence of phosphorus in steel is tolerated up to 0.02 mass %. Content of phosphorus in steel is preferably 0.018 mass % or less.
  • Sulfur is an element which exists as sulfide inclusion in steel and effectively improves machinability of the steel.
  • too high content of sulfur in steel deteriorates fatigue strength of the steel.
  • the upper limit of sulfur content in steel is to be 0.03 mass %.
  • Aluminum is an important element in terms of fixing nitrogen in steel as AlN to ensure a good hardenability-improving effect caused by boron.
  • Content of aluminum in steel need be at least 0.04 mass % in order to sufficiently obtain the good effect of boron.
  • content of Al in steel exceeding 0.10 mass % facilitates generation of Al 2 O 3 inclusion which harmfully affects fatigue strength of the steel. Accordingly, content of Al in steel is to be restricted to the range of 0.04 mass % to 0.10 mass %.
  • Chromium is a useful element which not only contributes to improving hardenability and temper softening resistancy of steel but also facilitates spheroidization of carbide therein.
  • Content of Cr in steel lower than 0.5 mass % cannot cause such good effects of Cr in a satisfactory manner, while content of Cr in steel exceeding 2.5 mass % possibly facilitates generation of retained austenite in a carburized portion of the steel to adversely affect fatigue strength thereof. Accordingly, Cr content in steel is to be restricted to the range of 0.5 mass % to 2.5 mass %.
  • the lower limit of Cr content in steel is preferably 0.6 mass % and the upper limit thereof is preferably 2.0 mass %.
  • Boron is the most important element in the present invention. Boron exists in a segregated manner at austenite grain boundaries of a steel material during quenching heat treatment, thereby improving hardenability and contributing to increase in hardness of the steel material. These good effects caused by boron allow contents of other hardness-enhancing elements in the steel material to be reduced, whereby deformation resistance is lowered and cold forgeability of the steel material improves. Content of boron in steel need be at least 0.0005 mass % in order to sufficiently cause these good effects of boron. However, too high content of boron in steel deteriorates toughness and forgeability of steel. Accordingly, the upper limit of boron content in steel is to be 0.0050 mass % and preferably 0.0030 mass %.
  • Nb 0.003 mass % to 0.080 mass %
  • Niobium forms NbC in steel and suppresses, by pinning effects, grain coarsening of austenite grains in the steel during carburizing heat treatment.
  • Content of Nb in steel need be at least 0.003 mass % in order to sufficiently obtain this good effect by niobium.
  • Nb content in steel exceeding 0.080 mass % results in precipitation of coarse NbC, thereby possibly deteriorating the effect of suppressing grain coarsening of austenite grains and/or possibly decreasing fatigue strength of the steel.
  • content of Niobium in steel is to be 0.080 mass % or less.
  • the lower limit of Nb in steel is preferably 0.010 mass % and the upper limit thereof is preferably 0.060 mass %.
  • Titanium is a component of which inclusion into steel is preferably avoided as best as possible. Titanium tends to be bonded to nitrogen to form coarse TiN.
  • the upper limit of Ti in steel is to be 0.003 mass % because titanium possibly coarsens carbide in a carburized surface layer and decreases fatigue strength of the steel.
  • Nitrogen is a component of which inclusion into steel is preferably avoided as best as possible. Content of nitrogen in steel is to be less than 0.008 mass % to ensure the good effect of improving hardenability by boron and reliably suppress formation of TiN.
  • the component composition of the case hardening steel may further include at least one element selected from Cu: 1.0 mass % or less, Ni: 0.50 mass % or less, Mo: 0.5 mass % or less, and V: .0.5 mass % or less in order to further improve hardenability.
  • Copper is an element which effectively improves hardenability and content thereof in steel is preferably at least 0.1 mass %.
  • the upper limit of Cu in steel is to be 1.0 mass %.
  • Ni, Mo and V are elements which effectively improve hardenability and toughness of steel and contents of Ni, Mo and V in steel are preferably at least 0.1 mass %, 0.05 mass % and 0.02 mass %, respectively.
  • the upper limits of contents of Ni, Mo and V are to be 0.50 mass %, respectively, because these elements are expensive.
  • the component composition of the case hardening steel may further include at least one element selected from Ca: 0.0005 mass % to 0.0050 mass % and Mg: 0.0002 mass % to 0.0020 mass % in order to control morphology of sulfide and improve machinability and cold forgeability of steel.
  • contents of Ca and Mg in steel need be at least 0.0005 mass % and 0.0002 mass %, respectively, in order to obtain the aforementioned good effects of Ca and Mg.
  • too high contents of Ca, Mg in steel result in formation of coarse inclusions, which may adversely affect fatigue strength of the steel.
  • the upper limits of contents of Ca and Mg in steel are to be 0.0050 mass % and 0.0020 mass %, respectively.
  • the remainder of the component composition is iron and incidental impurities.
  • a case hardening steel having the component composition described above is subjected to at first cold forming into the product shape and then carburizing treatment.
  • Carburizing treatment may be carried out under the conditions generally applied to a standard case hardening steel (such carburizing treatment will be referred to as "normal carburization” hereinafter).
  • the case hardening steel is retained under the conditions of carbon potential: 0.8 mass % to 1.1 mass %, temperature: 900°C or higher, and retention time: 3 to 7 hours, so that a carburized layer having carbon concentration of at least 0.7 mass % is formed in a surface layer ranging from a steel surface to 0.4 mm depth of the case hardening steel.
  • the case hardening steel in which the carburized layer has been formed is subjected to such conventional quench-and-temper process as is generally carried out for a standard case hardening steel.
  • the quench-and-temper process includes subjecting the case hardening steel to: quenching in oil at temperature in the range of 60°C to 140°C such that microstructure of the surface layer (the carburized layer) of the steel is rendered to martensite structure including 10% to 40% of retained austenite; and tempering at temperature in the range of 160°C to 200°C for 1 to 2 hours.
  • the temperature during formation of the carburized layer is preferably 900°C or higher in terms of avoiding prolonging time required for the carburized layer formation and preferably 950°C or lower in terms of avoiding any adverse effect on durability of a carburizing furnace.
  • the temperature of oil during quenching process is preferably 60°C or higher in terms of suppressing deformation of the steel material during the quenching process and preferably 140°C or lower in terms of reliably obtaining targeted microstructure (i.e. martensite structure including 10% to 40% of retained austenite) of steel to ensure satisfactory hardness of the steel.
  • Carbon concentration of a carburized layer obtained by normal carburization is less than 0.85 mass %.
  • the case hardening steel of the present invention is particularly suitable for super-carburization, in which carbon concentration in a carburized layer is increased to 0.85 mass % or higher to make carbides be precipitated, further harden the carburized layer and improve pitting fatigue strength thereof, rather than normal carburization.
  • the conventional case hardening steel generates too much coarse carbide and fails to further improve pitting fatigue strength after being subjected to super-carburization.
  • the case hardening steel of the present invention can suppress precipitation of coarse carbide and improve pitting fatigue strength in a case where carbon concentration in the carburized layer is increased to 0.85 mass % or higher.
  • carbon content of the surface layer region ranging from a steel surface to 0.4 mm depth thereof is at least 0.85 mass % and the maximum diameter of carbide formed in the surface layer region is 10 ⁇ m or less and the average particle diameter of the carbide is 4 ⁇ m or less after being subjected to carburization. It has been revealed that controlling the maximum diameter and the average particle diameter of carbide in the aforementioned specific ranges significantly improves pitting fatigue strength of the case hardening steel. Such a good effect of improving pitting fatigue strength as this cannot be expected beyond the aforementioned specific diameter ranges of carbide.
  • the carburizing heat treatment is preferably conducted under following conditions in order to obtain carbide satisfying the aforementioned requirements. That is, the carburizing heat treatment preferably includes: carburizing the case hardening steel by retaining the steel at carbon potential of 1.2 mass % to 2.5 mass % at temperature in the range of 930°C to 1050°C for 1 to 5 hours; then subjecting the case hardening steel to cooling to 550°C to 650°C, retention at temperature in the range of 830°C to 880°C for 30 minutes to 60 minutes, quenching in oil at temperature in the range of 60°C to 140°C, and preferably conducting tempering at temperature preferably in the range of 170°C to 200°C.
  • carburized layer as a surface layer of the case hardening steel, the carburized layer having the aforementioned steel microstructure constituted of martensite structure including 10% to 40% of retained austenite and also including finely dispersed carbide having the maximum diameter of 10 ⁇ m or less and the average particle diameter of 4 ⁇ m or less.
  • Each of steel samples having respective component compositions shown in Table 1 (the balance of each component composition is iron and incidental impurities) was processed by ingot casting, heated to temperature at 1150°C or higher, and formed into an intermediate material member having a square cross section (170mm ⁇ 170mm).
  • the intermediate material member was heated to temperature equal to or higher than (Ac 3 + 100°C) and hot rolled to a round bar having diameter of 60mm. Cold forgeability was then evaluated for the round bar sample thus obtained.
  • Example F 0,20 0,20 0,56 0,012 0,022 0,050 0,0035 1,30 0,0015 0,019 0,001 - - - - - 0,0006 Present
  • Example G 0,19 0,18 0,97 0,017 0,016 0,081 0,0065 1,20 0,0025 0,008 0,002 - - - - 0,0012 - Present
  • Example H 0,27 0,19 0,65 0,011 0,014 0,026 0,0064 1,10 0,0022 0,012 0,15 - - - - - - Comp
  • Example I 0,21 0,63 0,56 0,013 0,029 0,079 0,0055 1,12 0,0011 0,011 0,003 - 0,09 - - - - Comp.
  • Example J 0,22 0,38 0,92 0,009 0,018 0,015 0,0045 0,87 0,0025 0,005 0,001 - - 0,08 - - - Comp.
  • Example K 0,17 0,22 0,88 0,008 0,012 0,160 0,0071 1,40 0,0031 0,006 0,001 - - - - - 0,0011 Comp
  • Example L 0,22 0,11 0,93 0,014 0,029 0,067 0,0115 1,31 0,0029 0,010 0,002 - - - - - - Comp
  • Example M 0,16 0,26 0,77 0,014 0,016 0,066 0,0046 1,78 0,0002 0,015 0,001 0,07 0,08 - - 0,0017 - Comp.
  • Example N 0,24 0,06 0,79 0,015 0.017 0,064 0,0045 1,22 0,0016 0,114 0,002 - - - - - - Comp.
  • Example P 0,22 0,12 0,88 0,016 0,022 0,064 0,0022 1,11 0,0045 0,021 0,027 - - 0,15 - - - Comp.
  • Example Q 0,16 0,07 0,42 0,012 0,011 0,085 0,0035 3,31 0,0022 0,016 0,002 - - - - - - Comp.
  • Example R 0,22 0,21 1,55 0,016 0,019 0,074 0,0059 0,33 0,0019 0,019 0,001 - 0.10 - - 0,0012 - Comp.
  • Example S 0,22 0,1 1 0,98 0,014 0,015 0,077 0,0051 1,32 0,0084 0,012 0,002 - - - - - - Comp.
  • Example T 0,19 0,12 0,84 0,015 0,013 0,074 0.0043 1.45 0,0016 0,028 0,001 - 0,11 - - - - Present
  • Example U 0,18 0,23 0,55 0,015 0.013 0,074 0,0034 2,81 0,0012 0,022 0,001 0,13 - - - - - Comp.
  • Cold formability of the round bar sample was evaluated in terms of limit upset ratio and deformation resistance.
  • deformation resistance was determined by: collecting a test piece (diameter: 10mm, height: 15mm) from a region ranging from a steel surface to a diameter/4 position in the radial direction (a D/4 position) of each round bar sample; and then measuring compression load at 60% upset forging by using a 300t press according to the deformation resistance measuring method recommended by The Japan Society for Technology of Plasticity, based on end face confined compression.
  • the limit upset ratio was determined by carrying out compression processing of the test piece according to the method for measuring deformation resistance described above and regarding the upset ratio when an end portion of the test piece was cracked as "the limit upset ratio". Cold forgeability of a sample is evaluated to be good when the deformation resistance value is 899 MPa or less and the limit upset ratio (the limit cracking ratio) is at least 74%.
  • rotating bending fatigue test pieces and roller pitting fatigue test pieces were collected from the aforementioned D/4 position of each round bar sample.
  • the rotating bending fatigue test pieces were subjected to two different types of thermal processes, i.e. normal carburization and super-carburization for generating lots of carbide.
  • the roller pitting fatigue test pieces were also subjected to the two different types of thermal processes described above.
  • the normal carburization included: carburization at carbon potential of 1.1 mass % at 930°C for 7 hours; oil quenching at 60°C; and tempering at 170°C for 2 hours.
  • the super-carburization included: carburization at carbon potential of 2 mass % at 950°C for 5 hours; cooling to 600°C; retention at 850°C for 30 minutes; oil quenching at 60°C; and tempering at 170°C for 2 hours.
  • measurement of carbide after carburization included: etching a cut section with picral solution; observing an area ranging from a steel surface to 30 ⁇ m depth (6000 ⁇ m 2 ) by using a scanning electron microscope; and determining the maximum particle diameter and the average diameter of carbide through image analysis. Specifically, each carbide image was converted into a circle having the equal area and the maximum diameter and the average diameter of the circles thus obtained were regarded as "the maximum particle diameter” and "the average particle diameter" of the carbide, respectively. Carbide present in another depth range, i.e. a steel surface to the 0.4mm depth, of each sample was also observed.
  • Example 16 M 877 76 Super-carburization 11,5 3.8 1,18 726 2770 Comp Example 17 N 933 71 Super-carburization 9,4 3,4 1,15 746 2890 Comp.
  • Example 18 P 846 76 Super-carburization 15,1 4,9 1,13 746 2770 Comp Example 19 Q 975 68 Super-carburization 7,8 3,8 1,21 766 2890 Comp.
  • Example 20 R 889 75 Super-carburization 9,4 4,9 1,19 756 2890 Comp.
  • Example 21 S 902 69 Super-carburization 16,2 5,1 1,22 726 2770 Comp.
  • Example 22 T 847 77 Normal carburization - - 0.74 786 3010 Present Example 23 U 957 71 Normal carburization - - 0,72 746 2770 Comp.
  • Example * Underlined values: beyond the present invention or failing to meet the target values

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  • Chemical & Material Sciences (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
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  • Chemical Kinetics & Catalysis (AREA)
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Claims (3)

  1. Ein einsatzgehärteter Stahl mit einer Komponentenzusammensetzung bestehend aus
    C: 0,10 Massen-% bis 0,35 Massen-%;
    Si: 0,01 Massen-% bis 0,50 Massen-%;
    Mn: 0,40 Massen-% bis 1,50 Massen-%;
    P: 0,02 Massen-% oder weniger;
    S: 0,03 Massen-% oder weniger;
    Al: 0,04 Massen-% bis 0,10 Massen-%;
    Cr: 0,5 Massen-% bis 2,5 Massen-%;
    B: 0,0005 Massen-% bis 0,0050 Massen-%;
    Nb: 0,003 Massen-% bis 0,080 Massen-%;
    Ti: 0,003 Massen-% oder weniger;
    N: weniger als 0,0080 Massen-%; optional mindestens ein Element ausgewählt aus
    Cu: 1,0 Massen-% oder weniger,
    Ni: 0,50 Massen-% oder weniger,
    V: 0,5 Massen-% oder weniger,
    Ca: 0,0005 Massen-% bis 0,0050 Massen-%, und
    Mg: 0,0002 Massen-% bis 0,0020 Massen-%;
    wobei
    der Ausgleich Fe und zufällige Verunreinigungen sind
  2. Aufgekohltes Stahlmaterial, erhalten durch Aufkohlung des einsatzgehärteten Stahls nach Anspruch 1, wobei das aufgekohlte Stahlmaterial einen Kohlenstoffgehalt in einem Oberflächenschichtbereich von einer Stahloberfläche bis zu einer Tiefe von 0,4 mm von mindestens 0,7 Massen-% aufweist.
  3. Aufgekohltes Stahlmaterial, erhalten durch Aufkohlung des einsatzgehärteten Stahls nach Anspruch 1, wobei das aufgekohlte Stahlmaterial einen Kohlenstoffgehalt in einem Oberflächenschichtbereich von einer Stahloberfläche bis zu einer Tiefe von 0,4 mm von mindestens 0,85 Massen-% aufweist und wobei der Maximaldurchmesser und der durchschnittliche Teilchendurchmesser des Carbids in dem Oberflächenschichtbereich 10 µm oder weniger bzw. 4 µm oder weniger beträgt.
EP11736785.4A 2010-01-27 2011-01-26 Einsatzgehärteter stahl und aufgekohltes material Active EP2530178B1 (de)

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KR101705168B1 (ko) * 2015-04-20 2017-02-10 현대자동차주식회사 내구성이 향상된 침탄 합금강 및 이의 제조방법
JP6319212B2 (ja) * 2015-07-09 2018-05-09 Ｊｆｅスチール株式会社 歯車部品および歯車部品の製造方法
JP2017179394A (ja) * 2016-03-28 2017-10-05 株式会社神戸製鋼所 肌焼鋼
JP6460069B2 (ja) * 2016-05-31 2019-01-30 Ｊｆｅスチール株式会社 肌焼鋼およびその製造方法ならびに歯車部品の製造方法
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CN102770570A (zh) 2012-11-07
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WO2011093070A1 (ja) 2011-08-04
CN104480399A (zh) 2015-04-01
CN104480399B (zh) 2019-03-08
JP5760453B2 (ja) 2015-08-12
JP2011174176A (ja) 2011-09-08
KR20120099519A (ko) 2012-09-10
KR101671133B1 (ko) 2016-10-31
EP2530178A1 (de) 2012-12-05
JP2015096657A (ja) 2015-05-21

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