WO2010116670A1 - 浸炭鋼部品 - Google Patents
浸炭鋼部品 Download PDFInfo
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- WO2010116670A1 WO2010116670A1 PCT/JP2010/002264 JP2010002264W WO2010116670A1 WO 2010116670 A1 WO2010116670 A1 WO 2010116670A1 JP 2010002264 W JP2010002264 W JP 2010002264W WO 2010116670 A1 WO2010116670 A1 WO 2010116670A1
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/20—Carburising
- C23C8/22—Carburising of ferrous surfaces
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- 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
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- 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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
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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
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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
- C23C8/02—Pretreatment of the material to be coated
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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
- C23C8/80—After-treatment
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- 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
- C21D1/26—Methods of annealing
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- 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
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- 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
- C21D2261/00—Machining or cutting being involved
Definitions
- the present invention relates to a carburized steel part having excellent machinability before carburizing and static bending strength.
- FIG. 7 is a diagram showing the relationship between the depth from the surface and the Vickers hardness of the carburized steel part obtained by such treatment. As shown in FIG. 7, since the surface layer hardness can be increased by the above-described processing, for example, by performing the above-described processing on the gear component, high cycle bending fatigue strength and wear resistance of the gear component are achieved. Can be improved.
- Patent Documents 1 to 3 described in detail below disclose techniques for improving the static bending strength of carburized steel parts.
- C 0.1 to 0.3% by weight
- Mn 0.35 to 1.1% by weight
- Cr 0.1 to 1.1% by weight
- Mn + Cr 0.6 to 1.7%
- B 0.001 to 0.005 wt%, wherein the C content of the surface portion of the carburized hardened layer is 0.6 to 1.1. It discloses a carburized steel part having a weight percent and an area fraction of troostite in the carburized hardened layer of 5 to 50%.
- Patent Document 2 C: 0.1 to 0.3% by weight, Mn: 0.5 to 1.3% by weight, Cr: 0.1 to 1.1% by weight, Mn + Cr: 0.9 to 1.9
- carburized steel parts having an area fraction of troostite in the carburized hardened layer of 5 to 50% are disclosed.
- Patent Document 3 discloses a method of carburizing a molded product using an alloy steel material containing Ni of 0.5% or more and removing a region having a depth of 20 ⁇ m or more from the surface of the molded product after the carburizing treatment by electrolytic polishing or the like. Is disclosed.
- Patent Documents 1 to 3 described above cannot sufficiently improve the static bending strength.
- the technique for improving the static bending strength is generally not desirable from the viewpoint of machinability before carburizing because it is based on the improvement of the hardness of the base metal and the addition of a large amount of alloy elements. For this reason, it has been required to achieve both excellent carburizing machinability and excellent static bending strength.
- the present invention aims to provide a carburized steel part that is superior in machinability before carburizing and static bending strength to meet such a problem.
- the present invention employs the following means in order to solve the above-described problems.
- a first aspect of the present invention is a carburized steel part obtained by subjecting a base material to a cutting process and a carburizing process, wherein the base material has C: more than 0.3 to 0.6 % By mass, Si: 0.01 to 1.5% by mass, Mn: 0.3 to 2.0% by mass, P: 0.0001 to 0.02% by mass, S: 0.001 to 0.15% by mass , N: 0.001 to 0.03 mass%, Al: more than 0.06 to 0.3 mass%, O: 0.0001 or more and 0.005 mass%, containing iron and inevitable impurities
- the carburized steel part is a carburized steel part having a surface layer hardness of HV550 to HV800 and a core hardness of HV400 to HV550.
- the base material is Ca: 0.0002 to 0.005 mass%, Zr: 0.0003 to 0.005 mass%, Mg: 0.0003 to One or more chemical components of 0.005% by mass and Rem: 0.0001 to 0.015% by mass may be further contained.
- the base material may further contain a chemical component of B: 0.0002 to 0.005 mass%. .
- the base material includes Cr: 0.1 to 3.0% by mass, Mo: 0.1 to 1.
- One or more chemical components of 5% by mass, Cu: 0.1 to 2.0% by mass, and Ni: 0.1 to 5.0% by mass may be further contained.
- the base material includes Ti: 0.005 to 0.2 mass%, Nb: 0.01 to 0.1. It may further contain one or more chemical components of mass%, V: 0.03 to 0.2 mass%.
- the carburized steel part according to any one of (1) to (5) may be a gear.
- gears can be significantly reduced in size and weight without significantly increasing production costs due to deterioration of machinability before carburizing of carburized steel parts. CO 2 emissions can be reduced.
- FIG. 6 which shows the relationship between the depth from the surface of the carburized steel part of the present invention and the Vickers hardness with a solid line
- the surface layer hardness falls within the range of HV550 to HV800
- the core hardness is It was clarified that it is preferable to be within the range of HV400 to HV550.
- the broken line of FIG. 6 shows the hardness distribution of the conventional carburized steel member.
- the solid solution Al generated in the base material can improve the machinability of the base material before carburizing.
- a tool coated with a coating containing an oxide composed of a metal element having an affinity for oxygen of Al or less, that is, an oxide whose standard generation free energy has an absolute value of Al 2 O 3 or less When the cutting process is used, a chemical reaction is likely to occur at the contact surface between the tool and the steel material. As a result, it becomes easy to form an Al 2 O 3 coating on the tool surface layer, and it functions as a tool protection film. It was clarified that the tool life can be extended.
- a carburized steel part according to an embodiment of the present invention is manufactured by cutting and carburizing a base material containing C, Si, Mn, P, S, N, Al, and O.
- a base material containing C, Si, Mn, P, S, N, Al, and O.
- the preferable content of each chemical component will be described.
- % regarding content of a chemical component shows the mass%.
- C more than 0.3% and 0.6% or less
- C gives the core hardness of the parts subjected to carburizing and quenching treatment, and contributes to the improvement of static bending fatigue strength.
- the structure of the core part of the carburized and quenched part is mainly martensite.
- the hardness of the martensite after a carburizing quenching process becomes so high that there is much C amount.
- the yield ratio increases as the amount of C increases, through dispersion strengthening of fine carbides. In order to reliably obtain this effect, the C content needs to be more than 0.3%.
- the C content is preferably 0.32% or more, or 0.35% or more in order to make the core portion hardness HV450 or more.
- the C content exceeds 0.6%, the core hardness exceeds HV550 as described above, and also causes a sharp decrease in machinability before carburizing. It is necessary to be within the range of 0.6%.
- the C content is preferably 0.40% or less, and therefore the preferable range of C is 0.32 to 0.40%.
- Si 0.01-1.5%
- Si is an element effective for deoxidation of steel, and is an element effective for improving the temper softening resistance. Further, Si gives the core hardness of the parts that have been carburized and quenched through the improvement of the hardenability, and contributes to the improvement of the low cycle bending fatigue strength. If the Si content is less than 0.01%, the above-mentioned effects are insufficient. If the Si content exceeds 1.5%, the carburizing property is inhibited, so the Si content must be within the range of 0.01 to 1.5%. is there.
- Si has an effect of increasing the activity of C in the steel material, so that Si is within the range of 0.5 to 1.5%. It has the effect of suppressing the surface layer hardness and is effective in further improving the static bending strength.
- a preferable range of Si is 0.5 to 1.5%.
- Mn is an element effective for deoxidation of steel, and gives the core hardness of the carburized and quenched parts through improvement of hardenability, thereby contributing to improvement of static bending strength. If Mn is less than 0.3%, the effect is insufficient, and if it exceeds 2.0%, the above effect is saturated, so the amount of Mn needs to be within the range of 0.3 to 2.0%. .
- P 0.0001% to 0.02%
- P segregates at the austenite grain boundaries during carburizing, thereby causing the grain boundary fracture, thereby lowering the static bending strength. Therefore, its content needs to be limited to 0.02% or less.
- the preferred range is 0.01% or less.
- the preferable range of P is 0.0001% or more and 0.01% or less.
- a in FIG. 2 and A ′ in FIG. 3 show examples in which the static bending strength is reduced by the excessive addition of P.
- S (S: 0.001 to 0.15%) S is added for the purpose of improving the machinability before carburization by MnS formed in steel, but the effect is insufficient if it is less than 0.001%. On the other hand, if it exceeds 0.15%, the effect is saturated, and rather, grain boundary segregation occurs and grain boundary embrittlement occurs. For these reasons, it is necessary to keep the S content within the range of 0.001 to 0.15%. The preferred range is 0.01 to 0.1%.
- N combines with Al, Ti, Nb, V, etc. in the steel to form nitrides or carbonitrides, and suppresses coarsening of crystal grains. If N is less than 0.001%, the effect is insufficient. If it exceeds 0.03%, the effect is saturated, and in addition, undissolved carbonitride remains during hot rolling or hot forging heating. Therefore, it is difficult to increase the amount of fine carbonitride effective for suppressing the coarsening of crystal grains. Therefore, it is necessary to keep the N content within the range of 0.001 to 0.03%. The preferred range is 0.003 to 0.010%.
- FIG. 5 shows N limited to 0.008% or less and 0.02%, 0.04%, 0.08%, 0.1%, 0.18%, 0.24%, or 0.3. It is a figure which shows the machinability before carburizing of 8 types of base materials containing% Al. As FIG. 5 shows, it turns out that machinability before carburizing improves, so that Al content is large.
- the effect of improving the machinability before carburizing is that Al 2 O 3 formed on the tool surface by a chemical reaction between the solid solution Al present in the base material and the oxide layer (Fe 3 O 4 ) on the surface layer of the cutting tool. Based on the protective film effect.
- the Al content needs to be within the range of more than 0.06 to 0.3%.
- the preferred range is 0.075 to 0.25%. More preferably, it is 0.1 to 0.15%.
- O is an element that causes grain boundary segregation to easily cause grain boundary embrittlement, and forms hard oxide inclusions (for example, Al 2 O 3 ) in steel to easily cause brittle fracture. O needs to be limited to 0.005% or less. On the other hand, it is not preferable to make the O content lower than 0.0001% from the viewpoint of cost. Therefore, the preferable range of O is 0.0001% or more and 0.005% or less.
- the above-described base material may contain one or more of Ca, Zr, Mg, and Rem.
- the effect of improving the machinability before carburizing and the effect of reducing the anisotropy of the mechanical properties due to MnS can be obtained.
- desirable contents when these chemical components are contained will be described.
- Ca 0.0002 to 0.005%
- Ca improves the machinability before carburization by lowering the melting point of the oxide and softening it by increasing the temperature in the cutting environment. However, if it is less than 0.0002%, it has no effect and exceeds 0.005%. And CaS are produced in large amounts, and the machinability before carburizing is reduced. For this reason, it is desirable to keep the Ca content in the range of 0.0002 to 0.005%.
- Zr 0.0003 to 0.005%
- Zr is a deoxidizing element and generates an oxide, but also has an interrelationship with MnS by generating sulfides. Zr-based oxides tend to become nuclei for crystallization / precipitation of MnS. Therefore, it is effective for dispersion control of MnS.
- the amount of Zr added is preferably more than 0.003% in order to aim at spheroidization of MnS. However, in order to finely disperse, it is preferable to add 0.0003 to 0.005%.
- the latter is practically preferable from the viewpoint of production in terms of quality stability (component yield and the like), that is, 0.0003 to 0.005% in which MnS is finely dispersed. If it is 0.0002% or less, the effect of adding Zr is hardly observed.
- Mg is a deoxidizing element, which generates an oxide, but also has an interrelationship with MnS by generating sulfides. Mg-based oxides tend to become nuclei for crystallization / precipitation of MnS. Further, since the sulfide becomes a composite sulfide of Mn and Mg, the deformation is suppressed and spheroidized. Therefore, it is effective for dispersion control of MnS. However, if it is less than 0.0003%, there is no effect, and if it exceeds 0.005%, a large amount of MgS is generated, and the machinability before carburization is reduced. It is desirable to be within the range of ⁇ 0.005%.
- Rem (rare earth element) is a deoxidizing element, which generates a low melting point oxide, not only suppresses nozzle clogging during casting, but also dissolves or bonds in MnS, lowering its deformability, rolling and It also has the function of suppressing the elongation of the MnS shape during hot forging.
- Rem is an effective element for reducing anisotropy.
- the total amount of Rem is less than 0.0001%, the effect is not remarkable, and when Rem is added in an amount exceeding 0.015%, a large amount of Rem sulfide is generated, and the pre-carburization is performed. The machinability deteriorates. Therefore, when adding Rem, the content is made 0.0001 to 0.015%.
- B may be contained in the above-mentioned base material in order to improve static bending strength by improving hardenability and grain boundary strength.
- the preferable content when B is contained is as follows.
- B suppresses the grain boundary segregation of P, and contributes to the improvement of static bending strength through the improvement of its own grain boundary strength and intragranular strength, and the improvement of hardenability. If B is less than 0.0002%, the effect is insufficient, and if it exceeds 0.005%, the effect is saturated. Therefore, it is desirable to keep the content within the range of 0.0002 to 0.005%. The preferred range is 0.0005 to 0.003%.
- the above-described base material may contain one or more of Cr, Mo, Cu, and Ni in order to improve static bending strength by improving hardenability. Desirable contents when these chemical components are contained are as follows.
- Cr 0.1-3.0%
- Cr is an element effective for improving the static bending strength by giving the core hardness of a carburized and quenched part through improvement of hardenability. If Mn is less than 0.1%, the effect is insufficient, and if it exceeds 3.0%, the effect is saturated. Accordingly, it is desirable to keep the Cr content within the range of 0.1 to 3.0%.
- Mo 0.1-1.5%
- Mo is an element effective for improving the static bending strength by giving the core hardness of the parts subjected to carburizing and quenching through improvement of hardenability. If Mn is less than 0.1%, the effect is insufficient, and if it exceeds 1.5%, the effect is saturated. Therefore, it is desirable to keep the Mo amount within the range of 0.1 to 1.5%.
- Cu 0.1-2.0%
- Cu is an element effective for improving the static bending strength by giving the core hardness of a carburized and quenched part through improvement of hardenability. If Cu is less than 0.1%, the effect is insufficient, and if it exceeds 2.0%, the effect is saturated. Therefore, it is desirable to keep the amount of Cu within the range of 0.1 to 2.0%.
- Ni 0.1-5.0%
- Ni is an element effective for improving the static bending strength by giving the core hardness of the parts subjected to carburizing and quenching through improvement of hardenability. If Ni is less than 0.1%, the effect is insufficient, and if it exceeds 5.0%, the effect is saturated. Therefore, it is desirable to keep the amount of Ni within the range of 0.1 to 5.0%.
- the above-mentioned base material can prevent grain coarsening even when the carburizing temperature is increased and the time is increased with the aim of increasing the carburizing depth, that is, the austenite grains are refined by increasing the amount of carbonitride.
- one or more of Ti, Nb, and V may be contained. Desirable contents when these chemical components are contained are as follows.
- Ti 0.005 to 0.2%)
- Ti may be added in order to produce fine TiC and TiCS in the steel by addition, and thereby to refine the austenite grains during carburization.
- generating TiN is acquired. That is, the solid solution B can be secured. If Ti is less than 0.005%, the effect is insufficient. On the other hand, if it exceeds 0.2%, TiN-based precipitates increase and rolling fatigue characteristics deteriorate. For the above reasons, it is desirable to keep the content within the range of 0.005 to 0.2%. The preferred range is 0.01 to 0.1%.
- Nb 0.01 to 0.16%
- Nb carbonitride is generated, and coarsening of crystal grains is suppressed. If Nb is less than 0.01%, the effect is insufficient. On the other hand, if it exceeds 0.1%, machinability before carburizing is deteriorated, so 0.1% is made the upper limit.
- V 0.03-0.2%
- V adds to produce V carbonitride and suppresses coarsening of crystal grains. If V is less than 0.03%, the effect is insufficient. On the other hand, if it exceeds 0.2%, the machinability before carburizing is deteriorated, so 0.05% is made the upper limit.
- the base material of the present invention may contain impurities inevitably mixed in the manufacturing process in addition to the elements described above, but it is preferable that impurities are not mixed as much as possible.
- the surface layer hardness is the hardness of the carburized layer, it can be adjusted by adjusting the carbon potential during carburizing or adjusting the tempering temperature after carburizing and quenching.
- a steel part is subjected to a carburizing and quenching process at a carbon potential of 0.8, and then tempered at 150 ° C., and then a static bending test is performed. Therefore, when the static bending strength is lower than necessary, the surface potential hardness is decreased by decreasing the carbon potential to 0.7 or increasing the tempering temperature to 180 ° C., thereby improving the static bending strength. Adjust to.
- the core hardness is in the range of HV430 to HV550. More desirably, it is within the range of HV450 to HV550.
- the core hardness exceeds HV550, the toughness of the core portion is significantly reduced, and the static bending strength is reduced through an increase in the crack propagation speed of the core portion.
- B 1 , B 2 , and B 3 in FIG. 2 indicate the static bending strength of the carburized steel parts whose core hardness deviates from the above range
- the core part defined here is a part in which a small amount of C penetrates from the surface of the part by carburizing treatment according to the depth. Specifically, it refers to a portion that is 10% higher than the C content of the base material (0.22% when the C content of the base material is 0.20%) or less.
- a base material here is a steel material before carburizing treatment. Therefore, the core part can be identified by EPMA-C line analysis or the like. The core hardness can be adjusted by adjusting the C concentration of the base material and the hardenability by adding alloy elements.
- the effects of the present invention can be obtained by any method such as a gas carburizing method, a vacuum carburizing method, or a gas carbonitriding method that is generally a carburizing method.
- the carburized steel parts of the present invention are used for gear parts such as machine structural parts, differential gears, transmission gears, carburized shafts with gears, and are particularly useful for differential gears.
- a steel ingot having the chemical composition shown in Table 1 is forged to 35 mm, then subjected to soaking and normalization (however, adjusted to a ferrite-pearlite structure by adjusting cooling). As shown in FIG. 1 (excluding counterbore processing), rough processing was performed on a static bending test piece ( ⁇ 15) 3 having a parallel portion 1 and a notch (semicircular arc) 2 in the central recess.
- a cylindrical test piece having a diameter of 30 mm and a height of 21 mm was cut out and milled to obtain a drill cutting test piece.
- test piece No. Nos. 1 to 29 and 31 were carburized at 930 ° C. for 5 hours in a modified gas carburizing furnace, and were oil-quenched at 130 ° C.
- Specimen No. 30 was a carburizing treatment at 930 ° C. for 5 hours in a modified gas carburizing furnace, and oil quenching at 220 ° C. was performed.
- Specimen No. 1-30 were tempered at 150 ° C. for 1.5 hours after oil quenching.
- Specimen No. No. 31 was tempered at 120 ° C. for 1.5 hours after oil quenching.
- the carbon potential during the carburizing treatment is in the range of 0.5 to 0.8, and the tempering temperature is the test piece No.
- the surface layer hardness and the core hardness were adjusted by adjusting the temperature within the range of 150 to 300 ° C. except 31.
- a spot bending process 4 of 1 mm was applied to the test piece to produce a static bending test piece.
- the static bending test piece after rough machining has a shape excluding the dotted line in FIG. 1, and the static bending test piece after finishing is a seat corresponding to the dotted line in FIG. It is a shape that has been bored.
- Table 2 shows the hardness after the above-mentioned normalization and the material survey results after carburizing treatment (after carburizing quenching and tempering treatment).
- the pre-carburization machinability test a drill drilling test was performed on the test piece for drill cutting under the cutting conditions shown in Table 3, and the machinability before carburization of each steel material of the example and the comparative example was evaluated. At that time, as an evaluation index, a maximum cutting speed VL1000 (m / min) capable of cutting to a cumulative hole depth of 1000 mm was adopted in the drill drilling test.
- the static bending test was performed by bending a static bending test piece at four points. In this test, the test was carried out at a compression speed of 0.1 mm / min, and the maximum load up to breakage was determined to obtain the static bending strength. However, when the surface layer hardness was extremely low, the amount of plastic deformation on the outermost surface was remarkably increased. Therefore, the maximum load up to that point was defined as static bending strength.
- the results of static bending strength are shown in Table 2.
- test No. In addition to being excellent in static bending strength of 11 kN or more in Nos. 1 to 23, it became clear that machinability before carburization (VL1000) was excellent as 35 m / min or more.
- test No. of the comparative example. No. 24 had a poor static bending strength. This is because C of the steel material was less than 0.3%, which is the specified range of the present invention, and as a result, the core hardness was lower than the specified range of the present invention.
- Comparative test No. No. 25 had a poor static bending strength. This is because C of the steel material exceeded 0.6% which is the specified range of the present application, and as a result, the core hardness was higher than the specified range of the present invention.
- Comparative test No. No. 26 had poor static bending strength. This is due to the fact that Si in the steel material exceeded 1.5% of the specified range of the present invention, and thus carburization was hindered, resulting in lower than the surface layer hardness of the specified range of the present invention, and the amount of plastic deformation on the outermost surface. This is because the maximum load up to that point was evaluated as the static bending strength.
- Comparative test No. No. 27 had poor static bending fatigue strength. This is because P of the steel material exceeded 0.02% of the specified range of the present invention, and grain boundary fracture due to P grain boundary segregation was caused.
- Comparative test No. 28 and 29 had poor machinability before carburizing. This is because the effect of improving the machinability before carburizing by solute Al was not exhibited due to the fact that Al in the steel material was less than 0.06% of the specified range of the present invention.
- Comparative test No. No. 30 had a poor static bending fatigue strength. This is because the quenching oil was as high as 220 ° C., and as a result, quenching was insufficient, and the core hardness was lower than HV400 within the range specified in the present invention.
- Comparative test No. No. 31 had a poor static bending fatigue strength. This is because the tempering temperature was as low as 120 ° C., and as a result, the surface layer hardness exceeded HV800 defined in the present invention.
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Abstract
Description
特許文献1は、C:0.1~0.3重量%、Mn:0.35~1.1重量%、Cr:0.1~1.1重量%、Mn+Cr:0.6~1.7重量%、B:0.001~0.005重量%の化学成分を含有する母材から製造される浸炭鋼部品であって、浸炭硬化層の表面部のC量が0.6~1.1重量%であり、その浸炭硬化層におけるトルースタイトの面積分率が5~50%である浸炭鋼部品を開示している。
(6)上記(1)~(5)のいずれか1項に記載の浸炭鋼部品が歯車であってもよい。
上記(2)に記載の構成によれば、浸炭前被削性の改善効果やMnSに起因する機械的性質の異方性低減効果を得ることができる。
上記(3)に記載の構成によれば、焼入性や粒界強度の改善による静的曲げ強度の向上効果を得ることができる。
上記(4)に記載の構成によれば、焼入性の向上による静的曲げ強度向上効果を得ることができる。
上記(5)に記載の構成によれば、粒粗大化防止効果を得ることができる。
上記(6)に記載の構成によれば、優れた浸炭前被削性と優れた静的曲げ強度とを併せ持つ歯車を得ることができる。
また、本発明によれば、浸炭鋼部品の浸炭前被削性の劣化による生産コストの大幅な増加を招かずに、歯車の大幅な小型軽量化が可能となり、自動車の燃費向上とそれを通じたCO2排出量削減が可能となる。
Cは、浸炭焼入れ処理した部品の芯部硬さを与え、静的曲げ疲労強度の向上に寄与する。浸炭焼入れ処理した部品の芯部の組織はマルテンサイトが主体である。また、浸炭焼入れ処理後のマルテンサイトの硬さはC量が多いほど高くなる。また、同じ芯部硬さであってもC量が高いほうが微細炭化物の分散強化を通じて降伏比が増加する。この効果を確実に得るには、C量を0.3%超にする必要がある。更に静的曲げ疲労強度を向上させるため芯部硬さをHV450以上とさせるべく、C量を0.32%以上、又は0.35%以上とすることが好ましい。一方、C量は0.6%を超えると、上記のとおり、芯部硬さがHV550を超え、また、急激な浸炭前被削性の低下を招くため、C量を0.3%超~0.6%の範囲に収める必要がある。浸炭前被削性の観点からはC量は0.40%以下とするのが好ましいので、Cの好適範囲は0.32~0.40%である。
Siは、鋼の脱酸に有効な元素であり、焼戻し軟化抵抗を向上するのに有効な元素である。また、Siは、焼入れ性の向上を通じて浸炭焼入れ処理した部品の芯部硬さを与え、低サイクル曲げ疲労強度の向上に寄与する。Siは0.01%未満では上述の効果が不十分であり、1.5%を超えると浸炭性が阻害されるため、Si量を0.01~1.5%の範囲内に収める必要がある。一般的なカーボンポテンシャル0.7~1.0のガス浸炭法を採用した場合、Siは鋼材中のCの活量を増加させる影響を通じて、Siが0.5~1.5%の範囲内では表層部硬さを抑制する効果があり、静的曲げ強度の更なる向上に有効である。Siの好適範囲は0.5~1.5%である。
Mnは、鋼の脱酸に有効な元素であるとともに、焼入れ性の向上を通じて浸炭焼入れ処理した部品の芯部硬さを与え、静的曲げ強度の向上に寄与する。Mnは0.3%未満ではその効果が不十分であり、2.0%を超えると上述の効果が飽和するため、Mn量を0.3~2.0%の範囲内に収める必要がある。
Pは、浸炭時のオーステナイト粒界に偏析し、それにより粒界破壊を引き起こすことよって静的曲げ強度を低下させてしまうため、その含有量を0.02%以下に制限する必要がある。好適範囲は0.01%以下である。一方、Pの含有量を0.0001%より低くすることは、コストの観点から好適でない。従って、Pの好適範囲は0.0001%以上0.01%以下である。図2におけるA、及び図3におけるA’は、Pの過剰添加により静的曲げ強度が低下した例を示す。
Sは、鋼中で形成されるMnSによる浸炭前被削性の向上を目的として添加するが、0.001%未満ではその効果は不十分である。一方、0.15%を超えるとその効果は飽和し、むしろ粒界偏析を起こし粒界脆化を引き起こす。以上の理由から、Sの含有量を0.001~0.15%の範囲内に収める必要がある。好適範囲は0.01~0.1%である。
Nは、鋼中でAl、Ti、Nb、V等と結合して窒化物又は炭窒化物を生成し、結晶粒の粗大化を抑制する。Nは0.001%未満ではその効果が不十分であり、0.03%を超えるとその効果が飽和するのに加え熱間圧延又は熱間鍛造加熱時に未固溶の炭窒化物が残存し、結晶粒の粗大化を抑制するのに有効な微細な炭窒化物の増量が難しくなる。従って、Nの含有量を0.001~0.03%の範囲内に収める必要がある。好適範囲は0.003~0.010%である。
図5は、0.008%以下に制限されたNと、0.02%、0.04%、0.08%、0.1%、0.18%、0.24%、又は0.3%のAlとを含有する8種類の母材の浸炭前被削性を示す図である。図5に示されるように、Al含有量が大きいほど、浸炭前被削性が向上することがわかる。この浸炭前被削性向上効果は、母材中に存在する固溶Alと、切削工具の表層部の酸化層(Fe3O4)との化学反応により工具表面に形成されるAl2O3による保護膜効果に基づく。その反面、Alが多すぎるとAl2O3介在物のサイズが大きくなり、高サイクルの疲労強度に対しては劣位となる。従って、Alの含有量は、0.06超~0.3%の範囲内に収める必要がある。好適範囲は0.075~0.25%である。更に好ましくは、0.1~0.15%である。
Oは、粒界偏析を起こして粒界脆化を起こしやすくするとともに、鋼中で硬い酸化物系介在物(例えば、Al2O3)を形成して脆性破壊を起こしやすくする元素である。Oは0.005%以下に制限する必要がある。一方、Oの含有量を0.0001%より低くすることは、コストの観点から好適でない。従って、Oの好適範囲は0.0001%以上0.005%以下である。
Caは、酸化物を低融点化し、切削加工環境下の温度上昇により軟質化することで、浸炭前被削性を改善するが、0.0002%未満では効果が無く、0.005%を超えるとCaSを多量に生成し、浸炭前被削性を低下する。このためCa量を0.0002~0.005%の範囲に収めることが望ましい。
Zrは、脱酸元素であり、酸化物を生成するが、硫化物も生成することでMnSとの相互関係を有する元素である。Zr系酸化物はMnSの晶出/析出の核になりやすい。そのためMnSの分散制御に有効である。Zr添加量として、MnSの球状化を狙うためには0.003%を超えた添加が好ましいが、微細分散させるためには逆に0.0003~0.005%の添加が好ましい。製品としては後者のほうが、製造上、品質安定性(成分歩留まり等)の観点から後者、すなわちMnSを微細分散させる0.0003~0.005%の方が現実的に好ましい。0.0002%以下ではZr添加効果はほとんど認められない。
Mgは、脱酸元素であり、酸化物を生成するが、硫化物も生成することでMnSとの相互関係を有する元素である。Mg系酸化物はMnSの晶出/析出の核になりやすい。また、硫化物がMnとMgの複合硫化物となることで、その変形を抑制し、球状化する。そのためMnSの分散制御に有効であるが、0.0003%未満では効果が無く、0.005%を超えるとMgSを多量に生成し、浸炭前被削性が低下するためMg量を0.0003~0.005%の範囲に収めることが望ましい。
Rem(希土類元素)は、脱酸元素であり、低融点酸化物を生成し、鋳造時ノズル詰りを抑制するだけでなく、MnSに固溶又は結合し、その変形能を低下させて、圧延及び熱間鍛造時にMnS形状の伸延を抑制する働きもある。このように、Remは異方性の低減に有効な元素である。しかしながら、Rem含有量が総量で0.0001%未満の場合、その効果は顕著ではなく、また、Remを0.015%を超えて添加すると、Remの硫化物を大量に生成し、浸炭前被削性が悪化する。よって、Remを添加する場合は、その含有量を0.0001~0.015%とする。
Bは、Pの粒界偏析を抑制するとともに、それ自体の粒界強度と粒内強度の向上、及び焼入れ性の向上を通じて静的曲げ強度の向上に寄与する。Bは0.0002%未満ではその効果が不十分であり、0.005%を超えるとその効果は飽和する。従って、その含有量を0.0002~0.005%の範囲内に収めることが望ましい。好適範囲は0.0005~0.003%である。
Crは、焼入れ性の向上を通じて浸炭焼入れ処理した部品の芯部硬さを与え、静的曲げ強度の向上に有効な元素である。Mnは0.1%未満ではその効果が不十分であり、3.0%を超えるとその効果が飽和する。従って、Cr量を0.1~3.0%の範囲内に収めることが望ましい。
Moは、焼入れ性の向上を通じて浸炭焼入れ処理した部品の芯部硬さを与え、静的曲げ強度の向上に有効な元素である。Mnは0.1%未満ではその効果が不十分であり、1.5%を超えるとその効果が飽和する。従って、Mo量を0.1~1.5%の範囲内に収めることが望ましい。
Cuは、焼入れ性の向上を通じて浸炭焼入れ処理した部品の芯部硬さを与え、静的曲げ強度の向上に有効な元素である。Cuは0.1%未満ではその効果が不十分であり、2.0%を超えるとその効果が飽和する。従って、Cu量を0.1~2.0%の範囲内に収めることが望ましい。
Niは、焼入れ性の向上を通じて浸炭焼入れ処理した部品の芯部硬さを与え、静的曲げ強度の向上に有効な元素である。Niは0.1%未満ではその効果が不十分であり、5.0%を超えるとその効果が飽和する。従って、Ni量を0.1~5.0%の範囲内に収めることが望ましい。
Tiは、添加することによって鋼中で微細なTiC、TiCSを生成させ、これにより浸炭時のオーステナイト粒の微細化を図るために添加してもよい。また、Tiを添加する場合、鋼中でNと結合してTiNを生成することによるBNの析出防止効果が得られる。つまり、固溶Bを確保することができる。Tiは0.005%未満ではその効果が不十分である。一方、0.2%を越えるとTiN主体の析出物が多くなって転動疲労特性が低下する。以上の理由から、その含有量を0.005~0.2%の範囲内に収めることが望ましい。好適範囲は0.01~0.1%である。
Nbは、添加することによってNb炭窒化物を生成し、結晶粒の粗大化を抑制する。Nbは0.01%未満ではその効果が不十分である。一方、0.1%を超えると浸炭前被削性を劣化させるので0.1%を上限とする。
Vは、添加することによってV炭窒化物を生成し、結晶粒の粗大化を抑制する。Vは0.03%未満ではその効果が不十分である。一方、0.2%を超えると浸炭前被削性を劣化させるので0.05%を上限とする。
本発明者らは図2に示すように、表層部硬さHV550~HV800の範囲内において、表層部硬さが低いほど静的曲げ強度が向上することを明らかにした。また、本発明者らは、この理由が、表層部硬さが高いと表面から脆性破面の亀裂が発生し、その脆性破面が急速に伝播するためであることを、破損品の破面観察結果から明らかにした。この傾向はHV800を超えると顕著に現出する。このため、表層部硬さはHV800以下であることが好ましい。より好ましくはHV770以下である。表層部硬さが低い場合には、亀裂は同様に表面から発生するが、脆性破面の発生率が低いために亀裂の伝播速度が小さいので静的曲げ強度は向上する。しかし表層部硬さがHV550未満では最表層の塑性変形量が顕著に増大(歯車の場合には歯面の大幅な変形に相当)するため、歯車としての機能を損なうのに加え、最表層の硬さの低下は顕著に高サイクル曲げ疲労強度や耐摩耗性を損なってしまう。このため、表層部硬さをHV550~HV800の範囲内に収める必要がある。表層部硬さは浸炭層の硬さであるため、浸炭時のカーボンポテンシャルの調整や、浸炭焼入れ後の焼戻し温度の調整により調整することが可能である。調整の目安としては、鋼部品をカーボンポテンシャルを0.8で浸炭焼入れ処理を行い、その後、150℃で焼戻しを行った後に静的曲げ試験を実施する。そこで静的曲げ強度が所要よりも低い場合には、カーボンポテンシャルを0.7に低下、又は焼戻し温度を180℃に増加させることにより表層部硬さを低下させ、静的曲げ強度を向上させるように調整する。
本発明者らは図3に示すように、芯部硬さがHV400~HV550の範囲内において、芯部硬さが高いほど静的曲げ強度が向上することを明らかにした。本発明者らは、この理由が、芯部硬さが低いと、浸炭層直下の芯部が降伏して、それ以上の応力を受け持てず、浸炭層である鋼部品表面に発生する応力が大きくなるためであることを、破面観察等で明らかにした。従来、一般に用いられるJIS-SCr420、JIS-SCM420等よりも顕著に静的曲げ強度を向上させるには、HV400以上が必要であることから、芯部硬さは、HV400~HV550の範囲内に収める必要がある。望ましくは、芯部硬さはHV430~HV550の範囲内である。更に望ましくはHV450~HV550の範囲内である。なお芯部硬さがHV550を超えると、芯部の靭性が著しく低下してしまい、芯部の亀裂伝播速度が大きくなることを通じて静的曲げ強度が低下する。
2切欠(半円弧)
3静的曲げ試験片
4浸炭後座ぐり加工
Claims (6)
- 母材に対して切削加工処理及び浸炭処理を施して得られる浸炭鋼部品であって、
前記母材は、
C :0.3超~0.6質量%、
Si:0.01~1.5質量%、
Mn:0.3~2.0質量%、
P :0.0001~0.02質量%、
S :0.001~0.15質量%、
N :0.001~0.03質量%、
Al:0.06超~0.3質量%、
O :0.0001~0.005質量%、
の化学成分と、
鉄及び不可避的不純物を含む残部と、
を含有し、
前記浸炭鋼部品は、
表層部硬さがHV550~HV800であり、
芯部硬さがHV400~HV550である
ことを特徴とする浸炭鋼部品。 - 前記母材が、
Ca:0.0002~0.005質量%、
Zr:0.0003~0.005質量%、
Mg:0.0003~0.005質量%、
Rem:0.0001~0.015質量%、
の化学成分の1種以上を更に含有することを特徴とする請求項1に記載の浸炭鋼部品。 - 前記母材が、
B:0.0002~0.005質量%
の化学成分を更に含有することを特徴とする請求項1に記載の浸炭鋼部品。 - 前記母材が、
Cr:0.1~3.0%質量%、
Mo:0.1~1.5質量%、
Cu:0.1~2.0質量%、
Ni:0.1~5.0質量%、
の化学成分の1種以上を更に含有することを特徴とする請求項1に記載の浸炭鋼部品。 - 前記母材が、
Ti:0.005~0.2質量%、
Nb:0.01~0.1質量%、
V:0.03~0.2質量%、
の化学成分の1種以上を更に含有することを特徴とする請求項1に記載の浸炭鋼部品。 - 前記浸炭鋼部品が歯車であることを特徴とする請求項1~5のいずれか1項に記載の浸炭鋼部品。
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN2010800013389A CN102317490B (zh) | 2009-03-30 | 2010-03-29 | 渗碳钢部件 |
US12/989,970 US8801873B2 (en) | 2009-03-30 | 2010-03-29 | Carburized steel part |
EP10761376.2A EP2415892B1 (en) | 2009-03-30 | 2010-03-29 | Carburized steel part |
BRPI1001266-4A BRPI1001266B1 (pt) | 2009-03-30 | 2010-03-29 | Carburized steel part |
JP2010529027A JP4677057B2 (ja) | 2009-03-30 | 2010-03-29 | 浸炭鋼部品 |
KR1020107021698A KR101280203B1 (ko) | 2009-03-30 | 2010-03-29 | 침탄강 부품 |
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KR (1) | KR101280203B1 (ja) |
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BR (1) | BRPI1001266B1 (ja) |
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WO2012008405A1 (ja) * | 2010-07-14 | 2012-01-19 | 新日本製鐵株式会社 | 被削性に優れた機械構造用鋼 |
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US20120085209A1 (en) * | 2010-03-30 | 2012-04-12 | Toshiharu Aiso | Cutting method of steel for machine structural use |
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US9469883B2 (en) | 2009-05-13 | 2016-10-18 | Nippon Steel & Sumitomo Metal Corporation | Carburized steel part having excellent low cycle bending fatigue strength |
JP2011137214A (ja) * | 2010-01-04 | 2011-07-14 | Sumitomo Metal Ind Ltd | 差動歯車およびその製造方法 |
WO2011111269A1 (ja) * | 2010-03-10 | 2011-09-15 | 新日本製鐵株式会社 | 低サイクル曲げ疲労強度に優れた浸炭鋼部品 |
US20120085209A1 (en) * | 2010-03-30 | 2012-04-12 | Toshiharu Aiso | Cutting method of steel for machine structural use |
US8545137B2 (en) * | 2010-03-30 | 2013-10-01 | Nippon Steel & Sumitomo Metal Corporation | Cutting method of steel for machine structural use |
US9139894B2 (en) | 2010-07-14 | 2015-09-22 | Nippon Steel & Sumitomo Metal Corporation | Steel for machine structure exhibiting excellent machinability |
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US9797045B2 (en) | 2011-02-10 | 2017-10-24 | Nippon Steel & Sumitomo Metal Corporation | Steel for carburizing, carburized steel component, and method of producing the same |
CN103119189A (zh) * | 2011-02-10 | 2013-05-22 | 新日铁住金株式会社 | 渗碳用钢、渗碳钢部件及其制造方法 |
US9796158B2 (en) | 2011-02-10 | 2017-10-24 | Nippon Steel & Sumitomo Metal Corporation | Steel for carburizing, carburized steel component, and method of producing the same |
US10391742B2 (en) | 2011-02-10 | 2019-08-27 | Nippon Steel Corporation | Steel for carburizing, carburized steel component, and method of producing the same |
US10392707B2 (en) | 2011-02-10 | 2019-08-27 | Nippon Steel Corporation | Steel for carburizing, carburized steel component, and method of producing the same |
US9127342B2 (en) | 2011-09-19 | 2015-09-08 | Hyundai Motor Company | High-strength transmission gear and method of manufacturing the same |
JP2013185205A (ja) * | 2012-03-07 | 2013-09-19 | Kobe Steel Ltd | 肌焼用鋼部品 |
US20220349370A1 (en) * | 2021-04-30 | 2022-11-03 | Caterpillar Inc. | Components formed with high strength steel |
US11885289B2 (en) * | 2021-04-30 | 2024-01-30 | Caterpillar Inc. | Components formed with high strength steel |
Also Published As
Publication number | Publication date |
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TWI412607B (zh) | 2013-10-21 |
TW201042058A (en) | 2010-12-01 |
JPWO2010116670A1 (ja) | 2012-10-18 |
KR20100125367A (ko) | 2010-11-30 |
CN102317490A (zh) | 2012-01-11 |
EP2415892A4 (en) | 2017-05-03 |
US20110036463A1 (en) | 2011-02-17 |
US8801873B2 (en) | 2014-08-12 |
BRPI1001266B1 (pt) | 2017-12-19 |
EP2415892B1 (en) | 2018-05-02 |
TW201350591A (zh) | 2013-12-16 |
BRPI1001266A2 (pt) | 2016-02-16 |
EP2415892A1 (en) | 2012-02-08 |
CN102317490B (zh) | 2013-09-11 |
TWI494445B (zh) | 2015-08-01 |
JP4677057B2 (ja) | 2011-04-27 |
KR101280203B1 (ko) | 2013-06-28 |
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