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WO2011111269A1 - Composant en acier cémenté ayant une excellente résistance à la fatigue oligocyclique par flexion - Google Patents

Composant en acier cémenté ayant une excellente résistance à la fatigue oligocyclique par flexion Download PDF

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Publication number
WO2011111269A1
WO2011111269A1 PCT/JP2010/070516 JP2010070516W WO2011111269A1 WO 2011111269 A1 WO2011111269 A1 WO 2011111269A1 JP 2010070516 W JP2010070516 W JP 2010070516W WO 2011111269 A1 WO2011111269 A1 WO 2011111269A1
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Prior art keywords
fatigue strength
bending fatigue
low cycle
cycle bending
less
Prior art date
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Ceased
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PCT/JP2010/070516
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English (en)
Japanese (ja)
Inventor
修司 小澤
学 久保田
修 加田
元裕 西川
高志 田中
典正 常陰
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sanyo Special Steel Co Ltd
Nippon Steel Corp
Original Assignee
Sanyo Special Steel Co Ltd
Nippon Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from JP2010053555A external-priority patent/JP5530763B2/ja
Application filed by Sanyo Special Steel Co Ltd, Nippon Steel Corp filed Critical Sanyo Special Steel Co Ltd
Priority to US13/139,000 priority Critical patent/US20120060979A1/en
Priority to CN2010800294541A priority patent/CN102471842A/zh
Priority to KR1020117030663A priority patent/KR20120012837A/ko
Publication of WO2011111269A1 publication Critical patent/WO2011111269A1/fr
Anticipated expiration legal-status Critical
Priority to US14/014,983 priority patent/US9469883B2/en
Ceased legal-status Critical Current

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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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/58—Oils
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16H—GEARING
    • F16H55/00—Elements with teeth or friction surfaces for conveying motion; Worms, pulleys or sheaves for gearing mechanisms
    • F16H55/02—Toothed members; Worms
    • F16H55/06—Use of materials; Use of treatments of toothed members or worms to affect their intrinsic material properties

Definitions

  • the present invention relates to a carburized steel part excellent in low cycle bending fatigue strength.
  • Gears such as mechanical structural parts, differential gears, transmission gears, and carburized shafts with gears have low cycle fatigue (fatigue in the range of several hundred to several thousand cycles) due to the sudden start and stop of the vehicle. ) May be damaged.
  • improvement of low cycle fatigue strength is further desired for differential gears and transmission gears.
  • the steel parts are made of case-hardened steel with C: around 0.2% such as JIS SCr420, SCM420, etc. as steel materials, thereby ensuring the toughness of the core, carburizing and quenching, and low temperature around 150 ° C.
  • the surface has a tempered martensite structure with C: around 0.8%, and the high cycle bending fatigue strength and wear resistance are enhanced.
  • Patent Document 1 contains C: 0.1 to 0.3%, B: 0.005% or less, Si: 0.3% or less, P : Carburized parts limited to 0.03% or less and core hardness: HV350 or more are disclosed.
  • Patent Document 2 the sum of plastic deformation resistance and grain boundary strength calculated from the component composition is limited to C: 0.15 to 0.3%, Si: 0.5% or less, and P: 0.01% or less. The case hardening steel which raised low cycle fatigue strength by making more than a fixed value is disclosed.
  • Patent Document 3 C: 0.1 to 0.3%, B: 0.001 to 0.005%, Si: 0.5% or less, P: 0.03% or less,
  • the hardness of the core part A carburized gear excellent in low cycle fatigue strength of HV300 or more is disclosed.
  • C is 0.15 to 0.3%, B is 0.0003 to 0.005%, Si is 0.03 to 0.25%, and P is limited to 0.02% or less.
  • the carburized component which improved the low cycle impact fatigue characteristic by making the value relevant to the core hardness calculated from the component composition more than a fixed value is disclosed.
  • Patent Document 5 C: 0.1 to 0.4%, Si: 1.0% or less, Mn: more than 1.5 to 3%, P: 0.03% or less, S: 0.03% or less Cr: 0.3 to 2.5%, Al: 0.005 to 0.050%, Ti: 0.003% or less, O: 0.0015% or less, N: 0.025% or less, balance is inevitable
  • a carbonitrided bearing steel comprising impurities and Fe, having a surface hardness of 58 HRC or more after carbonitriding or subsequent secondary quenching and tempering, and a surface retained austenite amount of 20 to 50% is disclosed. .
  • Patent Document 6 C: 0.1 to 0.4%, Si: 0.02 to 1.3%, Mn: 0.3 to 1.8%, S: 0.001 to 0.15%, Al: 0.001 to 0.05%, N: 0.003 to 0.020%, P: 0.025% or less, O: 0.0025% or less, and Cr: 1.8% or less Mo: 1.5% or less, Ni: 3.5% or less, B: 0.006% or less, V: 0.5% or less, Nb: 0.04% or less, Ti: 0.2% or less
  • Patent Document 7 C: 0.1 to 0.4%, Si: 0.5% or less, Mn: 1.5% or less, P: 0.03% or less, S: 0.03% or less, Cr : 0.3-2.5%, Mo: 0.1-2.0%, V: 0.1-2.0%, Al: 0.050% or less, O: 0.0015% or less, N: 0.025% or less, V + Mo: 0.4 to 3.0%, balance Fe and inevitable impurities, steel subjected to carburizing quenching and tempering treatment, and surface layer C concentration after tempering treatment is 0.6 to Hydrogen embrittlement with 1.2%, surface hardness of HRC 58 or more and less than 64, and the proportion of fine V-type carbides having a particle size of less than 100 nm among the V-type carbides dispersed and precipitated on the surface layer is 80% or more
  • a case-hardened steel excellent in mold surface fatigue strength is disclosed.
  • the low cycle bending fatigue strength does not reach the level of low cycle
  • JP-A-8-92690 Japanese Patent Laid-Open No. 10-259450 International Publication WO02 / 44435 JP 2004-238702 A Japanese Patent Laying-Open No. 2005-042188 JP 2007-332438 A JP 2008-280583 A
  • Patent Documents 1 to 7 cannot answer the improvement in low cycle bending fatigue strength that is required today. Then, this invention makes it a subject to provide the carburized-steel components which the low cycle bending fatigue strength improved notably compared with the conventional low cycle bending fatigue strength.
  • the steel material further comprises B: 0.0002 to 0.005% by mass%, and is excellent in low cycle bending fatigue strength as described in (1) or (2) above Carburized steel parts.
  • the steel material is further in mass%, Mo: less than 0.1%, Cu: less than 0.1%, and Ni: less than 0.1% as one or more kinds as unavoidable components.
  • the steel material is one type of Mo: 0.1 to 1.5%, Cu: 0.1 to 2.0%, and Ni: 0.1 to 5.0% in mass%.
  • the steel material further contains one or two kinds of Nb: 0.01 to 0.2% and V: 0.03 to 0.2% by mass%.
  • the steel material is one type of Ca: 0.0002 to 0.005%, Zr: 0.0003 to 0.005%, and Mg: 0.0003 to 0.005% by mass%.
  • gears such as differential gears for automobiles can be greatly reduced in size and weight, and as a result, the fuel efficiency of the automobile is improved, and , CO 2 emission can be reduced.
  • FIG. 1 is a diagram showing a low cycle bending fatigue test piece and a low cycle bending fatigue test method.
  • FIG. 2 is a diagram showing the effect of compressive residual stress (MPa) on 500 cycle bending fatigue strength (kN).
  • FIG. 3 is a diagram showing the influence of the grain boundary oxide layer depth ( ⁇ m) on the 500 cycle bending fatigue strength (kN).
  • FIG. 4 is a diagram showing the influence of surface hardness (HV) on 500 cycle bending fatigue strength (kN).
  • FIG. 5 is a diagram showing the influence of core hardness (HV) on 500 cycle bending fatigue strength (kN).
  • C 0.1 to 0.6%
  • the core structure is a hardened structure mainly composed of martensite, and the hardened martensite becomes harder as the amount of C increases.
  • C is made 0.1 to 0.6%.
  • C is preferably 0.2% or more, and more preferably more than 0.3%.
  • C is preferably 0.4% or less.
  • it is effective to apply compressive residual stress.
  • the core of C around 0.2% first expands in the martensitic transformation, and then the carburized layer of C: around 0.8% expands in the martensitic transformation. Compressive stress remains near the surface of the steel part.
  • Si is an element that enhances hardenability, increases the core hardness of the steel part after carburizing and quenching, and contributes to the improvement of low cycle bending fatigue strength. If it is less than 0.01%, the effect of addition is insufficient. On the other hand, if it exceeds 1.5%, the carburizing property is inhibited, so Si is made 0.01 to 1.5%.
  • Si increases the activity of C in the steel material in the range of 0.5 to 1.5%. Therefore, it is an element effective for further improving the low cycle bending fatigue strength because it acts to suppress the surface hardness. Therefore, Si is preferably 0.5 to 1.5%.
  • Mn 0.3 to 2.0%
  • Mn is an element effective for deoxidation of steel materials, and is an element that improves the hardenability of steel materials, increases the core hardness of steel parts after carburizing and quenching, and contributes to the improvement of low cycle bending fatigue strength. . If it is less than 0.3%, the effect of addition is insufficient. On the other hand, if it exceeds 2.0%, the effect of addition is saturated, so Mn is set to 0.3 to 2.0%. Preferably, it is 0.8 to 1.5%.
  • P 0.02% or less P is an impurity, and segregates at austenite grain boundaries during carburizing, causing grain boundary fracture and reducing low cycle bending fatigue strength. Therefore, P is limited to 0.02% or less.
  • S 0.001 to 0.15%
  • S is an element that forms MnS in the steel and contributes to improvement of machinability. If it is less than 0.001%, the effect of addition is insufficient. On the other hand, if it exceeds 0.15%, the effect of addition is saturated and segregates at the grain boundary to cause grain boundary embrittlement.
  • 0.001 to 0.15% Preferably it is 0.01 to 0.1%.
  • N 0.001 to 0.03%
  • N is an element that forms a nitride or carbonitride that binds to Al, Ti, Nb, V, and the like in the steel material and has an effect of suppressing coarsening of crystal grains.
  • Al is an element added for the purpose of deoxidation of steel materials. If it is less than 0.001%, the effect of addition is insufficient. On the other hand, if it exceeds 0.06%, the effect of addition is saturated, so Al is made 0.001 to 0.06%. Preferably, the content is 0.01 to 0.04%.
  • O 0.005% or less
  • O is inevitably contained, and segregates at the grain boundaries to easily cause grain boundary embrittlement, and forms hard oxide inclusions that cause brittle fracture in the steel material. It is an element that is easy to do.
  • O is made 0.005% or less. Preferably it is 0.002% or less.
  • the steel material of the present invention contains B for further improving the low cycle bending fatigue strength (20 kN or more).
  • B 0.0002 to 0.005%
  • B is an element that suppresses the grain boundary segregation of P and increases the grain boundary strength, intragranular strength, and hardenability, and contributes to the improvement of low cycle bending fatigue strength (20 kN or more).
  • the steel material of the present invention further contains Cr in order to improve hardenability and further improve low cycle bending fatigue strength.
  • Cr 1.20 to 3.0% Cr is an element that improves the hardenability of the steel material, increases the core hardness of the steel part after carburizing and quenching, and contributes to the improvement of low cycle bending fatigue strength. If it is less than 1.20%, the effect of addition is insufficient.
  • the steel according to the present invention contains Ti in order to prevent the crystal grains from becoming coarse and the low cycle fatigue strength from deteriorating during high temperature carburizing.
  • Ti 0.005 to 0.2%
  • Ti is an element that generates fine TiC and / or TiS in a steel material. Due to the presence of TiC and / or TiS, austenite grains can be stably refined in high-temperature carburization at a carburizing temperature of 980 ° C. or higher, or for a long time of carburizing for 10 hours or longer. Deterioration of fatigue strength can be prevented.
  • Ti is an element that combines with N in the steel material to generate TiN, prevents precipitation of BN, and contributes to securing solid solution B. If the content is less than 0.005%, the effect of addition is insufficient. On the other hand, if the content exceeds 0.2%, a large amount of TiN-based precipitates are precipitated and the rolling fatigue characteristics are deteriorated. 005 to 0.2%. Preferably it is 0.01 to 0.1%. In the steel material of the present invention, Mo, Cu, and Ni inevitably mixed are limited to less than 0.1%. Preferably, it is limited to 0.05% or less, more preferably 0.01% or less.
  • Mo, Cu, and Ni are elements that have the effect of increasing the hardenability and increasing the low cycle bending fatigue strength, and contain one or more of the required amounts of Mo, Cu, and Ni. May be.
  • Mo: 0.1 to 1.5% Mo is an element that improves the hardenability of the steel material, increases the core hardness of the steel part after carburizing and quenching, and contributes to the improvement of low cycle bending fatigue strength. If it is less than 0.1%, there is no effect. On the other hand, if it exceeds 1.5%, the effect of addition is saturated, so Mo is made 0.1 to 1.5%. Preferably it is 0.3 to 1.2%.
  • Cu 0.1 to 2.0%
  • Cu is an element that improves the hardenability of the steel material, increases the core hardness of the steel part after carburizing and quenching, and contributes to the improvement of low cycle bending fatigue strength. If it is less than 0.1%, the effect of addition is insufficient. On the other hand, if it exceeds 2.0%, the effect of addition is saturated, so Cu is made 0.1 to 2.0%. Preferably it is 0.3 to 1.5%.
  • Ni 0.1-5.0%
  • Ni is an element that improves the hardenability of the steel material, increases the core hardness of the steel part after carburizing and quenching, and contributes to the improvement of low cycle bending fatigue strength. If it is less than 0.1%, there is no effect.
  • the steel according to the present invention may further contain one or two of Nb and V in order to prevent crystal grains from becoming coarse during low temperature carburization and deterioration of low cycle fatigue strength.
  • Nb 0.01 to 0.2%
  • Nb is an element that generates Nb carbonitride in steel. Because of the presence of Nb carbonitrides, austenite grains can be stably refined in high-temperature carburization with a carburizing temperature of 980 ° C. or higher and long-term carburizing with a carburizing time of 10 hours or longer. Strength deterioration can be prevented.
  • V 0.03-0.2%
  • V is an element that generates V carbonitride in the steel material. Because of the presence of V carbonitride, austenite grains can be stably refined in high-temperature carburization at a carburizing temperature of 980 ° C. or higher, or in long-term carburizing for a carburizing time of 10 hours or longer, so low cycle fatigue Strength deterioration can be prevented. If it is less than 0.03%, the effect of addition is insufficient.
  • the steel material of the present invention may contain a required amount of one or more of Ca, Zr, and Mg for improving machinability.
  • Ca 0.0002 to 0.005%
  • Ca is an element that lowers the melting point of oxides in steel materials. The low melting point oxide is softened by the temperature rise in the cutting environment, and improves the machinability of the steel material. If it is less than 0.0002%, there is no effect of addition. On the other hand, if it exceeds 0.005%, a large amount of CaS is generated and the machinability of the steel material is lowered. %.
  • Zr 0.0003 to 0.005%
  • Zr is an element that deoxidizes a steel material to generate an oxide, and also generates a sulfide. Sulfide contributes to the improvement of machinability in cooperation with MnS. Since Zr-based oxides serve as nuclei for MnS crystallization / precipitation, Zr is also an effective element for controlling the dispersion of MnS. Zr is added in an amount exceeding 0.003% for spheroidizing MnS. Conversely, in order to finely disperse MnS, 0.003 to 0.005% is added.
  • Mg is an element that deoxidizes a steel material to generate an oxide, and also generates a sulfide. Sulfide contributes to the improvement of machinability in cooperation with MnS. Mg-based oxides serve as nuclei for crystallization / precipitation of MnS, and sulfides become composite sulfides of Mn and Mg, thereby suppressing deformation of composite sulfides and making them spheroidized.
  • the surface hardness is set to HV550 to HV800 (see “ ⁇ ⁇ ” in the figure).
  • HV600 to HV750 is preferable, and HV620 to HV720 is more preferable.
  • the surface hardness exceeds HV800, the toughness of the surface is remarkably lowered, the propagation speed of cracks is increased, and the low cycle bending fatigue strength is lowered. Since the surface hardness is the hardness of the carburized structure forming the carburized layer, the surface hardness can be adjusted by adjusting the carbon potential during carburizing and the tempering temperature after carburizing and quenching.
  • a steel part is carburized and quenched at a carbon potential of 0.8, then tempered at 150 ° C., and then a low cycle bending fatigue test is performed. If the low cycle bending fatigue strength is lower than the required value, The carbon potential is lowered to 0.7, or the tempering temperature is raised to 180 ° C. to reduce the surface hardness, thereby improving the low cycle bending fatigue strength.
  • Core hardness: HV400 to HV500 The inventors investigated the influence of the core hardness (HV) on the 500 cycle bending fatigue strength (kN) in the range of the core hardness HV270 to HV650. The result is shown in FIG. From FIG.
  • the core hardness is in the range of HV400 to HV500, and the higher the core hardness is, the more the low cycle bending fatigue strength is improved.
  • the core hardness is low, the core (hardened structure) directly under the carburized layer yields, and the carburized layer cannot receive stress more than the stress when yielded. It has been found that the stress on the surface of the steel part increases.
  • the core hardness is required to be HV400 or more, so the core hardness is HV400 to HV500.
  • a core part is a location where C which penetrates from the surface of a steel part reaches by carburizing treatment. For example, it is a portion from a location where the material C increases by 10% (0.22% when the material C is 0.20%) to the material C.
  • the core can be identified by EPMA-C line analysis or the like.
  • the carburizing method does not need to use a special method, and the effects of the present invention are exhibited even when a gas carburizing method, a vacuum carburizing method, a gas carbonitriding method, or the like, which is a general carburizing method, is used.
  • a gas carburizing method a vacuum carburizing method, a gas carbonitriding method, or the like, which is a general carburizing method, is used.
  • the carburized structure is responsible for the surface hardness
  • the hardened structure is responsible for the core hardness, so the component composition is adjusted to give the steel the required carburizability and hardenability.
  • the core hardness can be adjusted separately. This point is also a feature of the present invention.
  • the conditions in the examples are one example of conditions used for confirming the feasibility and effects of the present invention, and the present invention is based on this one example of conditions. It is not limited.
  • the present invention can adopt various conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.
  • Steel materials having the composition shown in Tables 1 and 2 were forged and then subjected to soaking and normalization to produce a roughing test piece for a low cycle bending fatigue test and a roughing test piece for a wear test. .
  • Test No. 1 to 21 (invention example), test no. 23 to 25 (comparative examples) and test no.
  • the rough-processed test pieces 28 to 44 were subjected to carburizing treatment at 930 ° C. for 5 hours in a modified gas carburizing furnace, and then subjected to oil quenching at 130 ° C.
  • Specimen No. About the rough processing test piece of 26 (comparative example) carburizing treatment of 930 ° C. ⁇ 5 hours was performed in a modified gas carburizing furnace, and then oil quenching at 220 ° C.
  • the carbon potential during the carburizing treatment was adjusted in the range of 0.5 to 0.8, and the tempering temperature was adjusted in the range of 150 to 300 ° C. to adjust the surface hardness and core hardness.
  • the low cycle bending fatigue test is a four-point bending that applies a load 2 with a stress ratio of 0.1 to a 13 mm square low cycle bending fatigue test piece 1 having a notch X with a sine wave at a frequency of 1 Hz.
  • a fatigue test was performed.
  • the frequency of 1 Hz (about 0.01 s ⁇ 1 in terms of strain rate) is smaller than the strain rate actually applied to the automobile gear.
  • the repetition rate affects the fatigue test value when the strain rate is 10 s ⁇ 1 or more. This is a region, and 10 s ⁇ 1 is much larger than the strain rate actually applied to the automobile gear, so there is no problem in the evaluation with the frequency of 1 Hz.
  • the stress ratio of an actual automobile gear is 0, but the reason for setting the stress ratio to 0.1 in this test is to prevent the test piece from slipping during unloading during the test.
  • the low cycle bending fatigue strength is low. This is because the component composition of the steel is within the scope of the present invention, but the core hardness exceeds HV550.
  • the reason why the core hardness exceeds HV550 is that the amount of C is relatively high at 0.6% and the temperature of the quenching oil is as low as 20 ° C.
  • gears such as a differential gear for automobiles can be significantly reduced in size and weight. It becomes possible to improve fuel consumption and reduce CO 2 emission. Therefore, the effect of the present invention is extremely remarkable, and the present invention has great industrial applicability.

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  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Abstract

L'invention porte sur un composant en acier cémenté, ayant une excellente résistance à la fatigue oligocyclique par flexion, qui est obtenu par cémentation au carbone d'un matériau de type acier, qui contient 0,1-0,6 % en masse de C, 0,01-1,5 % en masse de Si, 0,3-2,0 % en masse de Mn, 0,02 % en masse ou moins de P, 0,001-0,15 % en masse de S, 0,001-0,03 % en masse de N, 0,001-0,06 % en masse d'Al et 0,005 % en masse ou moins d'O, le complément étant essentiellement constitué de fer et des impuretés inévitables, puis revenu du matériau de type acier. Le composant en acier cémenté est caractérisé en ce qu'il a une dureté superficielle de HV 550 à HV 800, et une dureté de noyau de HV 400 à HV 500.
PCT/JP2010/070516 2009-05-13 2010-11-11 Composant en acier cémenté ayant une excellente résistance à la fatigue oligocyclique par flexion Ceased WO2011111269A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
US13/139,000 US20120060979A1 (en) 2009-05-13 2010-11-11 Carburized steel part having excellent low cycle bending fatigue strength
CN2010800294541A CN102471842A (zh) 2010-03-10 2010-11-11 低循环弯曲疲劳强度优良的渗碳钢部件
KR1020117030663A KR20120012837A (ko) 2010-03-10 2010-11-11 저사이클 굽힘 피로 강도가 우수한 침탄강 부품
US14/014,983 US9469883B2 (en) 2009-05-13 2013-08-30 Carburized steel part having excellent low cycle bending fatigue strength

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JP2010-053555 2010-03-10
JP2010053555A JP5530763B2 (ja) 2009-05-13 2010-03-10 低サイクル曲げ疲労強度に優れた浸炭鋼部品

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US13/139,000 A-371-Of-International US20120060979A1 (en) 2009-05-13 2010-11-11 Carburized steel part having excellent low cycle bending fatigue strength
US14/014,983 Continuation US9469883B2 (en) 2009-05-13 2013-08-30 Carburized steel part having excellent low cycle bending fatigue strength

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WO2011111269A1 true WO2011111269A1 (fr) 2011-09-15

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WO2015137085A1 (fr) * 2014-03-13 2015-09-17 Ntn株式会社 Dispositif d'entraînement à moteur dans roue

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