WO2019142947A1 - Composant d'acier de palier carburé, et barre d'acier pour composant d'acier de palier carburé - Google Patents

Composant d'acier de palier carburé, et barre d'acier pour composant d'acier de palier carburé Download PDF

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WO2019142947A1
WO2019142947A1 PCT/JP2019/001916 JP2019001916W WO2019142947A1 WO 2019142947 A1 WO2019142947 A1 WO 2019142947A1 JP 2019001916 W JP2019001916 W JP 2019001916W WO 2019142947 A1 WO2019142947 A1 WO 2019142947A1
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bearing steel
steel
mass
carburized bearing
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PCT/JP2019/001916
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Japanese (ja)
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達也 小山
慶 宮西
根石　豊
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日本製鉄株式会社
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Priority to CN201980008192.1A priority Critical patent/CN111601908B/zh
Priority to JP2019566549A priority patent/JP6881613B2/ja
Priority to KR1020207021935A priority patent/KR102373224B1/ko
Priority to US16/963,151 priority patent/US20200340072A1/en
Publication of WO2019142947A1 publication Critical patent/WO2019142947A1/fr

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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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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    • C21—METALLURGY OF IRON
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • 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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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
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    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
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    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present disclosure relates to a carburized bearing steel part and a steel bar for the carburized bearing steel part.
  • Patent Document 1 discloses a technique for suppressing the bulged portion of the indentation periphery by increasing the amount of retained austenite on the rolling surface. Further, Patent Document 1 states that the amount of retained austenite is in the range of 20% to 45%.
  • Patent Document 2 discloses that the shot peening process on bearing steel parts is softened, that is, the compressive residual stress is reduced to suppress the occurrence of micro cracks generated at the time of shot peening. And, in Patent Document 2, it is disclosed that the indentation life is improved by suppressing the occurrence of a minute crack.
  • Patent Documents 3 to 5 disclose techniques relating to bearing steel parts. Specifically, it is as follows.
  • the precipitation amount of AlN is limited to 0.01% or less, the equivalent circle diameter is more than 20 ⁇ m, the aspect ratio is more than 3 and the sulfide density d (pieces / mm 2 ) and the content of S [
  • S] (% by mass) satisfies d ⁇ 1700 [S] +20.
  • production of the coarse grain of skin-hardening steel is prevented by controlling content of AlN, a sulfide, and S, and it is excellent in the cold workability, machinability, and the fatigue characteristic after carburizing hardening. Is disclosed.
  • Patent Document 5 discloses a bearing steel in which all the oxide inclusions contained in the steel have a particle diameter of 15 ⁇ m or less and particles of 10 ⁇ m or more are less than 2% of the whole. Patent Document 5 discloses that high strength, long life and high heat resistance are realized by controlling the particle size of oxide inclusions.
  • Patent Document 1 Japanese Patent Application Laid-Open Publication No. 64-55423
  • Patent Document 2 Japanese Patent Application Laid-Open Publication No. 2006-329319
  • Patent Document 3 International Publication WO 2010-116555 Publication
  • Patent Document 4 Japanese Patent Application Laid-Open Publication No. 2010-196114
  • Patent Document 5 Japanese Patent Application Laid-Open No. 5-140696
  • an object of the present disclosure is to provide a carburized bearing steel part having excellent indentation life while maintaining the surface hardness equal to that of a general bearing steel part, and a carburized bearing steel part suitable for obtaining the carburized bearing steel part It is providing a bar stock.
  • the above-mentioned subject includes the following means. ⁇ 1> Internal chemical composition from the surface of carburized bearing steel parts to a depth of 2.00 mm, In mass%, C: 0.15 to 0.25%, Si: 0.70 to 1.50%, Mn: 0.40 to 1.50%, Cr: 0.15 to 1.50%, Mo: 0.001 to 0.150%, S: 0.001 to 0.030%, N: 0.004 to 0.020%, Ca: 0.0002 to 0.0100% Al: 0.001 to 0.010%, O: 0 to 0.005%, P: 0 to 0.030%, Ni: 0 to 3.00%, Cu: 0 to 1.00%, Co: 0 to 3.00%, W: 0 to 1.00%, V: 0 to 0.30%, Ti: 0 to 0.300%, Nb: 0 to 0.300%, B: 0 to 0.0050% Pb: 0 to 0.50%, Bi: 0 to 0.50%, Mg: 0 to 0.0100%, Zr: 0
  • ⁇ 2> Internal chemical composition from the surface of carburized bearing steel parts to a depth of 2.00 mm, In mass%, Ni: 0.01 to 3.00%, Cu: 0.01 to 1.00%, Co: 0.01 to 3.00%, W: 0.01 to 1.00%, V: 0.01 to 0.30%, Ti: 0.001 to 0.300%, Nb: 0.001 to 0.300%, and B: 0.0001 to 0.0050%
  • the carburized bearing steel component as described in ⁇ 1> which contains 1 type, or 2 or more types of.
  • ⁇ 3> Internal chemical composition from the surface of carburized bearing steel parts to a depth of 2.00 mm, In mass%, Pb: 0.01 to 0.50%, Bi: 0.01 to 0.50%, Mg: 0.0001 to 0.0100%, Zr: 0.0001 to 0.0050%, Te: 0.0001 to 0.1000%, Rare earth elements: 0.0001 to 0.0050%
  • ⁇ 4> The carburized bearing steel component according to any one of ⁇ 1> to ⁇ 3>, wherein the C content of the carburized layer on the rolling contact surface is 0.60 to 1.10% by mass%.
  • a carburized bearing steel part excellent in indentation life while maintaining the surface hardness equal to that of a general bearing steel part, and a bar steel for a carburized bearing steel part suitable for obtaining the carburized bearing steel part Can provide
  • FIG. 1 is a schematic surface view showing a cylindrical rolling fatigue test piece whose outer dimension is ⁇ 12 mm ⁇ 22 mm.
  • a numerical range represented using “to” means a range including numerical values described before and after “to” as the lower limit value and the upper limit value. Further, a numerical range in which “super” or “less than” is added to the numerical values described before and after “to” means a range that does not include these numerical values as the lower limit value or the upper limit value. Moreover, “%” means "mass%” about content of the element of a chemical composition.
  • the carburized bearing steel part according to the present embodiment (hereinafter, also simply referred to as “bearing steel part”) has a predetermined chemical component, and in any part cross section, the equivalent circle diameter is 5 ⁇ m or more, CaO, Al 2 O includes 3 and SiO 2, and CaO, with Al 2 O 3 and the content of Al 2 O 3 to the total mass of SiO 2 is 50 percent by mass or more oxides (hereinafter, "equivalent circle diameter of 5 ⁇ m or more and The number density of Al 2 O 3 content is also referred to as “50% by mass or more oxide”) is 3.0 pieces / cm 2 or less, and the Vickers hardness of 50 ⁇ m depth from the rolling surface is 750 or more And the compressive residual stress of the rolling surface is 900 MPa or more.
  • the bearing steel component according to the present embodiment With the above-described configuration, becomes a bearing steel component having an excellent indentation life while maintaining the surface hardness equal to that of a general bearing steel component.
  • the bearing steel component according to the present embodiment was found by the following findings.
  • the present inventors carried out the following evaluation in order to realize a bearing steel part having an excellent indentation life while maintaining the surface hardness equal to or higher than that of a general bearing steel part. Specifically, with respect to bearing steels whose chemical compositions have been systematically changed, evaluation of indentation life was carried out when various processing processes were combined to make bearing steel parts. As a result, the following findings (1) to (2) were obtained.
  • the depression life reduction is caused by a crack generated from the raised surface of the indentation periphery.
  • (2) Select a steel material that has a circle equivalent diameter of 5 ⁇ m or more and a small number of oxides with a content of Al 2 O 3 of 50% by mass or more, and further compression residual stress by shot peening on the rolling surface of parts. By applying the crack, the crack is suppressed, and the indentation life can be improved.
  • the improvement of the indentation life is a mechanism that does not use retained austenite, that is, a mechanism that utilizes the effect of compressive residual stress and the effect of suppressing microcracks, and a large amount of retained austenite is not required. It also has the advantage of not letting it happen.
  • the bearing steel component according to the present embodiment is a bearing steel component having an excellent indentation life while maintaining the surface hardness equivalent to that of a general bearing steel component. And since the bearing steel parts which concern on this embodiment have the outstanding indentation life, they can be used also in a foreign material mixing environment.
  • the C content affects the hardness of the non-carburized area of the bearing steel parts.
  • the lower limit value of the C content is made 0.15%.
  • the upper limit value of the C content is made 0.25%.
  • the lower limit of the C content is preferably 0.17%, more preferably 0.18%.
  • the upper limit of the C content is preferably 0.24%, more preferably 0.23%.
  • Si 0.70 to 1.50%
  • Si is an element effective for deoxidation of steel and affecting the composition of oxides, and also an element effective for imparting strength in a high temperature environment necessary for bearing steel parts. If the Si content is less than 0.70%, the effect is insufficient. In addition, when the Si content exceeds 1.50%, an oxide containing Si appears and causes a crack during shot peening. For the above reasons, the Si content needs to be in the range of 0.70 to 1.50%.
  • the preferable lower limit of the Si content is 0.75%, and more preferably 0.80%. Further, the lower limit of the Si content may be more than 0.90% or 1.0%.
  • the upper limit of the Si content is preferably 1.40%, more preferably 1.20%.
  • Mn 0.40 to 1.50%
  • Mn is an element effective to impart the necessary strength and hardenability to the steel. If the Mn content is less than 0.40%, this effect is insufficient. If the Mn content exceeds 1.50%, retained austenite becomes large after carburizing and quenching, and the hardness decreases. For the above reasons, the Mn content needs to be in the range of 0.40 to 1.50%.
  • the preferable lower limit of the Mn content is 0.45%, and more preferably 0.5%.
  • the upper limit of the Mn content is preferably 1.40%, more preferably 1.30%.
  • Cr 0.15 to 1.50% Cr is an element effective to impart the necessary strength and hardenability to the steel. If the Cr content is less than 0.15%, the effect is insufficient. When the Cr content exceeds 1.50%, the effect is saturated. For the above reasons, the Cr content needs to be in the range of 0.15 to 1.50%.
  • the preferable lower limit of the Cr content is 0.18%, more preferably 0.20%.
  • the upper limit of the Cr content is preferably 1.45%, more preferably 1.40%.
  • Mo 0.001 to 0.150%
  • Mo is an effective element for improving the fatigue strength of the steel because Mo suppresses segregation of P at grain boundaries in addition to imparting necessary hardenability. If the Mo content is less than 0.001%, this effect is insufficient. When the Mo content exceeds 0.150%, the effect is saturated. For the above reasons, the Mo content needs to be in the range of 0.001 to 0.150%.
  • the preferable lower limit of the Mo content is 0.010%, more preferably 0.020%.
  • the preferable upper limit of the Mo content is 0.140%, and more preferably 0.130%.
  • S forms MnS in the steel, thereby improving the machinability of the steel.
  • S content equivalent to that of a general steel for machine structural use. From the above reasons, the content of S needs to be in the range of 0.001 to 0.030%.
  • the preferable lower limit of the S content is 0.002%, more preferably 0.003%.
  • the upper limit of the S content is preferably 0.025%, more preferably 0.020%.
  • N 0.004 to 0.020%
  • N is an element which is unavoidably mixed, but it has a grain refining effect by forming a compound with Al, Ti, V, Cr or the like. Therefore, it is necessary to add N 0.004% or more. However, when the N content exceeds 0.020%, the compound becomes coarse, and the crystal grain refining effect can not be obtained. Due to the above reasons, the N content needs to be in the range of 0.004 to 0.020%.
  • the preferred lower limit of the N content is 0.0045%, and more preferably 0.005%.
  • the upper limit of the N content is preferably 0.015%, more preferably 0.012%.
  • Ca 0.0002 to 0.0100%
  • Ca is an element effective for deoxidation of steel and reducing the content of Al 2 O 3 in the oxide. If the Ca content is less than 0.0002%, this effect is insufficient. When the Ca content exceeds 0.0100%, a large amount of coarse oxides containing Ca appear, which causes a reduction in rolling fatigue life. For the above reasons, the Ca content needs to be in the range of 0.0002 to 0.0100%.
  • the preferable lower limit of the Ca content is 0.0003%, and more preferably 0.0005%.
  • the upper limit of the Ca content is preferably 0.0080%, more preferably 0.0060%.
  • Al 0.001 to 0.010%
  • Al crystallizes in the steel as Al 2 O 3 and affects the cracks generated at the time of shot peening and the generation of cracks at indentations and bulges. Therefore, the Al content needs to be limited to 0.010% or less.
  • the upper limit of the Al content is preferably 0.009%, more preferably 0.007%.
  • the lower limit of the Al content is 0.001% because it is always mixed as an impurity such as an auxiliary material used at the time of production.
  • O 0 to 0.005%
  • O is an element that affects the formation of a crack during shot peening and a crack at a raised portion because it forms an oxide in steel.
  • the O content needs to be limited to 0.005% or less.
  • the upper limit of the O content is preferably 0.003% or less, more preferably 0.002%.
  • P 0 to 0.030% P segregates at austenite grain boundaries during heating before carburizing and quenching, thereby reducing the fatigue strength. Therefore, it is necessary to limit the P content to 0.030% or less.
  • the upper limit of the P content is preferably 0.025% or less, more preferably 0.023%.
  • the lower the P content the better, so the lower limit of the P content is 0%. That is, P may not be contained. However, if P is removed more than necessary, the manufacturing cost will increase. Therefore, the substantial lower limit of the P content should be 0.004%.
  • the bearing steel part according to the present embodiment is further substituted from Fe, and Ni, Cu, Co, W, V, Ti, Nb, and B are used instead. It may contain one or more selected from the group consisting of That is, the lower limit of the content of these elements is 0%. And when making these elements contain, let the upper limit of content of an element be an upper limit of the range mentioned later.
  • the content of each element is preferably more than 0% and not more than the upper limit of the range described later, and more preferably the range described later.
  • Ni 0.01 to 3.00%
  • Ni is an element effective to impart the necessary hardenability to the steel. If the Ni content is less than 0.01%, this effect may be insufficient. Therefore, the Ni content is preferably 0.01% or more. If the Ni content exceeds 3.00%, the amount of retained austenite increases after carburizing and quenching, and the hardness may decrease. From the above reasons, the upper limit of the Ni content is 3.00%. The upper limit of the Ni content is preferably 2.00%, more preferably 1.80%. The lower limit of the preferable Ni content is 0.10%, more preferably 0.30%.
  • Cu 0.01 to 1.00%
  • Cu is an element effective for improving the hardenability of steel. If the Cu content is less than 0.01%, this effect may be insufficient. Therefore, the Cu content is preferably 0.01% or more. When the Cu content exceeds 1.00%, hot ductility may be reduced. Therefore, the upper limit of the Cu content is 1.00%. The upper limit of the Cu content may be 0.50%, 0.30%, or 0.20%. When Cu is contained to obtain the above-mentioned effect, the preferable lower limit of the Cu content is 0.05%, and more preferably 0.10%.
  • Co 0.01 to 3.00%
  • Co is an element effective for improving the hardenability of steel. If the Co content is less than 0.01%, this effect may be insufficient. Therefore, the Co content is preferably 0.01% or more. When the Co content exceeds 3.00%, the effect may be saturated. Therefore, the upper limit of the Co content is 3.00%.
  • the upper limit of the Co content may be 1.00%, 0.50%, or 0.20%.
  • the preferable lower limit of the Co content is 0.05%, and more preferably 0.10%.
  • W 0.01 to 1.00% W is an element effective for improving the hardenability of steel. If the W content is less than 0.01%, this effect may be insufficient. Therefore, the W content is preferably 0.01% or more. When the W content exceeds 1.00%, the effect may be saturated. Therefore, the upper limit of the W content is set to 1.00%. The upper limit of the W content may be 0.50%, 0.30%, or 0.20%. When W is contained to obtain the above-mentioned effect, the preferable lower limit of the W content is 0.05%, and more preferably 0.10%.
  • V 0.01 to 0.30%
  • V is an element which forms a compound with C and N and brings about a grain refining effect. If the V content is less than 0.01%, this effect may be insufficient. Therefore, the V content is preferably 0.01% or more. When the V content exceeds 0.30%, the compound becomes coarse, and the grain refining effect may not be obtained. Therefore, the upper limit of the V content is 0.30%. The upper limit of the V content may be 0.20%. When V is contained to obtain the above-mentioned effect, the preferable lower limit of the V content is 0.10%, more preferably 0.15%.
  • Ti 0.001 to 0.300%
  • Ti is an element that forms Ti-based precipitates such as fine TiC, (Ti, Nb) C and TiCS in steel and brings about a grain refining effect. If the Ti content is less than 0.001%, this effect may be insufficient. Therefore, the Ti content is preferably 0.001% or more. When the Ti content exceeds 0.300%, the effect may be saturated. From the above reasons, the content of Ti is set to 0.300% or less. The upper limit of the Ti content is preferably 0.250%, more preferably 0.200%.
  • Nb 0.001 to 0.300%
  • Nb is an element that produces (Ti, Nb) C in steel and brings about a grain refining effect. If the Nb content is less than 0.001%, this effect may be insufficient. Therefore, the Nb content is preferably 0.001% or more. When the Nb content exceeds 0.300%, the effect may be saturated. From the above reasons, the content of Nb is made 0.300% or less. The upper limit of the Nb content is preferably 0.250%, more preferably 0.200%.
  • B 0.0001 to 0.0050%
  • B has the function of suppressing grain boundary segregation of P.
  • B also has the effect of improving grain boundary strength and intragranular strength, and the effect of improving hardenability, and these effects improve the fatigue strength of the steel. If the B content is less than 0.0001%, this effect may be insufficient. Therefore, the B content is preferably 0.0001% or more. When the B content exceeds 0.0050%, the effect may be saturated. For the above reasons, the B content is made 0.0050% or less.
  • the upper limit of the B content is preferably 0.0045%, more preferably 0.0040%.
  • the chemical composition of the bearing steel component according to the present embodiment is, further, at least one selected from the group consisting of Pb, Bi, Mg, Zr, Te and rare earth elements (REM) instead of part of Fe. May be contained. That is, the lower limit of the content of these elements is 0%. And when making these elements contain, let the upper limit of content of an element be an upper limit of the range mentioned later.
  • the content of each element is preferably more than 0% and not more than the upper limit of the range described later, and more preferably the range described later.
  • Pb 0.01 to 0.50%
  • Pb is an element that improves machinability by melting and embrittlement during cutting. If the Pb content is less than 0.01%, this effect may be insufficient. Therefore, the Pb content is preferably 0.01% or more. On the other hand, when added in excess, the productivity may be reduced. Therefore, the upper limit of the Pb content is 0.50%. The upper limit of the Pb content may be 0.30%, 0.20%, or 0.10%. When Pb is contained to obtain the above-mentioned effect, the preferable lower limit of the Pb content is 0.02%, more preferably 0.05%.
  • Bi 0.01 to 0.50% Bi is an element that improves machinability by finely dispersing sulfides. If the Bi content is less than 0.01%, this effect may be insufficient. Therefore, the Bi content is preferably 0.01% or more. On the other hand, if it is added excessively, the hot workability of the steel may be deteriorated and the hot rolling may become difficult. Therefore, the upper limit of the Bi content is 0.50%. The upper limit of the Bi content may be 0.20%, 0.10%, or 0.05%. When Bi is contained to obtain the above-mentioned effect, the preferable lower limit is 0.02%, more preferably 0.05%.
  • Mg 0.0001 to 0.0100%
  • Mg is a deoxidizing element and forms an oxide in the steel. Furthermore, Mg-based oxides formed by Mg tend to be nuclei of crystallization and / or precipitation of MnS. Further, the sulfide of Mg causes MnS to be spheroidized by becoming a composite sulfide of Mn and Mg. Thus, Mg is an element effective in controlling the dispersion of MnS and improving the machinability. If the Mg content is less than 0.0001%, this effect may be insufficient. Therefore, the Mg content is preferably 0.0001% or more.
  • the upper limit of the Mg content is made 0.0100%.
  • the upper limit of the Mg content is preferably 0.0080%, more preferably 0.0050%.
  • the preferable lower limit of the Mg content is 0.0005%, more preferably 0.0010%.
  • Zr 0.0001 to 0.0500%
  • Zr is a deoxidizing element and forms an oxide. Furthermore, the Zr-based oxide formed by Zr tends to be a nucleus of crystallization and / or precipitation of MnS. Thus, Zr is an element effective to control the dispersion of MnS and to improve the machinability. If the Zr content is less than 0.0001%, this effect may be insufficient. Therefore, the Zr content is preferably 0.0001% or more. However, if the amount of Zr exceeds 0.0050%, the effect may be saturated. Therefore, when Zr is contained to obtain the above-described effect, the upper limit of the Zr content is set to 0.0050%. The upper limit of the Zr content is preferably 0.0400%, more preferably 0.0100%. The preferable lower limit of the Zr content is 0.0005%, more preferably 0.0010%.
  • Te 0.0001 to 0.1000% Since Te promotes the spheroidization of MnS, it improves the machinability of the steel. If the Te content is less than 0.01%, this effect may be insufficient. Therefore, the Te content is preferably 0.01% or more. When the Te content exceeds 0.1000%, the effect may be saturated. Therefore, when Te is contained to obtain the above-described effect, the upper limit of the Te content is 0.1000%.
  • the preferred upper limit of the Te content is 0.0800%, more preferably 0.0600%.
  • the upper limit of the Te content may be 0.0100%, 0.0070%, or 0.0050%.
  • the preferred lower limit of the Te content is 0.0005%, more preferably 0.0010%.
  • Rare earth elements 0.0001 to 0.0050%
  • the rare earth elements form sulfides in the steel, and the sulfides become precipitation nuclei of MnS to promote the formation of MnS, thereby improving the machinability of the steel. If the total content of rare earth elements is less than 0.0001%, this effect may be insufficient. Therefore, the total content of the rare earth elements is preferably 0.0001% or more. However, if the total content of the rare earth elements exceeds 0.0050%, the sulfides become coarse, which may lower the fatigue strength of the steel. Therefore, in the case of containing the rare earth element to obtain the above-mentioned effect, the upper limit of the total content of the rare earth elements is set to 0.0050%. The upper limit of the total content of the rare earth elements is preferably 0.0040%, more preferably 0.0030%. The preferable lower limit of the total content of the rare earth elements is 0.0005%, more preferably 0.0010%.
  • the rare earth element is obtained by adding yttrium (Y) and scandium (Sc) to 15 elements from lanthanum (La) having atomic number 57 in the periodic table to lutetium (Lu) having atomic number 71. It is a generic term for elements.
  • the content of the rare earth element means the total content of one or more of these elements.
  • the chemical composition of the bearing steel part according to the present embodiment may further contain one or two selected from the group consisting of Sn and In, instead of part of Fe. That is, the lower limit of the content of these elements is 0%. And when making these elements contain, let the upper limit of content of an element be an upper limit of the range mentioned later.
  • the content of each element is preferably more than 0% and not more than the upper limit of the range described later, and more preferably the range described later.
  • Sn 0.01% to 2.0% Sn embrittles the ferrite and extends the tool life, and also has the effect of improving the surface roughness after cutting.
  • the Sn content is preferably 0.01% or more. Moreover, even if it contains Sn exceeding 2.0%, the effect is saturated. Therefore, when it contains Sn, let Sn content be 2.0% or less.
  • In 0.01% to 0.50% In is an element that improves machinability by melting and embrittlement during cutting. If the In content is less than 0.01%, this effect may be insufficient. Therefore, the In content is preferably 0.01% or more. On the other hand, when added in excess, the productivity may be reduced. Therefore, the upper limit of the In content is 0.50%. The upper limit of the In content may be 0.30%, 0.20%, or 0.10%. When In is contained to obtain the above effect, the lower limit of the In content is more preferably 0.02%, further preferably 0.05%.
  • the bearing steel part according to the present embodiment contains the above-described alloy component, and the balance contains Fe and impurities.
  • elements other than the above-mentioned alloy components for example, elements such as Sb, Ta, As, H, Hf, Zn, etc.
  • the mixing amount is the characteristics of the steel Is acceptable as long as it does not affect the
  • the bearing steel part according to the present embodiment is a carburized steel bearing steel part subjected to a carburizing treatment.
  • the C content of the carburized layer on the rolling surface of the steel bearing steel part is preferably 0.60 to 1.10%, and 0.65 to 1.05%. More preferable.
  • the C content of the carburized layer is an average C content at a position from the surface to a depth of 50 ⁇ m on the rolling surface of the steel bearing steel part.
  • the number density of oxides having a circle equivalent diameter of 5 ⁇ m or more and a content of Al 2 O 3 of 50% by mass or more will be described.
  • the inventors used a steel material having different types and amounts of oxide, and the relationship between oxide and indentation life investigated.
  • the influence of the type and amount of oxide species constituting the oxide was examined.
  • the proportion of Al 2 O 3 , CaO, and SiO 2 affects the indentation life, and the Al relative to the total mass of the three oxides. It was found that the content of 2 O 3 was strongly correlated with the indentation life. That is, in the oxide, Al 2 O 3, CaO, and also contain oxides other than SiO 2, Al 2 O 3, CaO, and the content of Al 2 O 3 to the total mass of SiO 2 is It was found that there was a strong correlation to the indentation life.
  • the shape and number of oxides that affect the indentation life were examined. As a result, it was found that the number density of oxides having a circle equivalent diameter of 5 ⁇ m or more correlates with the indentation life. Therefore, with regard to the content of Al 2 O 3 and the number density of oxides with a circle-equivalent diameter of 5 ⁇ m or more, which greatly affect the indentation life, the plots of the ordinate and the abscissa represent the circle-equivalent diameters. Good indentation life can be obtained in a region where the number density of oxides with a content of Al 2 O 3 of 5 ⁇ m or more and a content of Al 2 O 3 of 50 mass% or more is 3.0 pieces / cm 2 or less. It was found that the trace life decreased.
  • the preferable upper limit of the number density of oxides having a content of Al 2 O 3 of 50% by mass or more is 2.0 particles / cm 2 , and more preferably 1.5 particles / cm 2 .
  • the lower limit is 0 / cm 2 since no oxide is preferably present.
  • the number density of oxides is a value measured by the method described in [Example] except for the selection of the observation field of view.
  • the observation field of view should be 4 cm 2 in total of the area of the observation part of the cut surface.
  • Vickers hardness 50 ⁇ m deep from the rolling surface will be described.
  • the hardness of the level of bearing steel parts generally used for automobiles that is, a hardness of about 750 in Vickers hardness is required.
  • the hardness of the surface that is, the Vickers hardness at a depth of 50 ⁇ m from the rolling surface needs to be 750 or more.
  • the Vickers hardness becomes brittle if it becomes too high, it is necessary to make the upper limit 1050.
  • Vickers hardness is 1000, more preferably 950.
  • Vickers hardness is the value measured by the method described in [Example] except a cutting position.
  • the cutting position varies depending on the part shape, but may be a cross section cut perpendicularly to the surface of the transfer portion.
  • the compressive residual stress on the rolling surface has the effect of suppressing the occurrence of a crack from the raised portion of the indentation edge and improving the indentation life.
  • the compressive residual stress of the rolling surface needs to be 900 MPa or more.
  • the compressive residual stress on the rolling contact surface is preferably as high as possible.
  • the upper limit of the compressive residual stress of the rolling surface is 2000 MPa.
  • compressive residual stress is the value measured by the method described in [Example].
  • the metallographic structure of bearing steel parts will be described.
  • the bearing steel component according to the present embodiment can be obtained, for example, by performing carburizing, quenching and tempering. Therefore, the metallographic structure of the bearing steel part is constituted of, for example, a surface portion (that is, a carburized layer) having a carburized surface and a gradient of C concentration, and a core portion having the same C concentration as the base material before carburizing.
  • the metallographic structure of the surface layer (that is, the carburized layer) is exemplified by a metallographic structure consisting of tempered martensite, retained austenite, and the balance (such as bainite, ferrite, cementite, etc.).
  • the metal structure of a core part can illustrate the metal structure which consists of a tempered martensite and the remainder (a bainite, a ferrite, a pearlite, etc.).
  • the metallographic structure of the core portion is a metallographic structure inside from a depth of 2.00 mm from the surface of the bar steel for bearing steel parts.
  • the carburized bearing steel part steel bar according to the present embodiment suitable for obtaining the bearing steel parts according to the present embodiment (hereinafter, also referred to as “bearing steel parts steel bar”) is as follows.
  • the steel bar for bearing steel parts according to the present embodiment has the same chemical composition as the bearing steel parts according to the present embodiment, and has an equivalent circle diameter of 5 ⁇ m or more in any cross section of the steel bar, CaO, Al 2 O 3 and SiO
  • the number density of oxides having a content of Al 2 O 3 of 50% by mass or more based on the total mass of CaO, Al 2 O 3 and SiO 2 is 3.0 pieces / cm 2 or less.
  • the method of measuring the number density of oxides is the same as the method of measuring the number density of oxides in the bearing steel part according to the present embodiment.
  • the metallographic structure of the steel bar for bearing steel parts mainly includes ferrite (for example, at an area ratio of 60% or more), and can be exemplified by the metallographic structure consisting of pearlite, bainite, and the remaining portion.
  • the metallographic structure of the steel bar for bearing steel parts is a metallographic structure inside the surface at a depth of 2.00 mm from the surface of the steel bar for bearing steel parts.
  • the bearing steel part having the above metal structure may be manufactured, for example, as follows. First, primary refining is performed in the converter using iron ore or scrap-based raw materials. Si is added to the molten steel extracted from the converter, and then Al is added to carry out deoxidation treatment. After the deoxidation treatment, the ladle refining method and secondary refining by the refining method using a vacuum processing apparatus are adjusted to a molten steel component having the above-described chemical composition. It is preferable to continuously cast the component-adjusted molten steel into a steel ingot.
  • the number density of the above-mentioned oxides can be controlled.
  • the SiO 2 component is not mixed in the oxide as inclusions. This is because Si or SiO 2 has a reducing action.
  • the molten steel temperature in the tundish is superheated at 5 to 200 ° C., and electromagnetic stirring is performed in the mold.
  • the steel ingot is subjected to slabbing, and is worked into a predetermined cross-sectional shape by hot rolling, and then cooled to obtain a steel bar for bearing steel parts.
  • the cooling rate after the hot rolling may be controlled in the range of 0.1 to 5 ° C./sec at an average cooling rate between 800 ° C. and 300 ° C. of the surface temperature of the steel material.
  • carburizing, quenching and tempering are performed by forming the obtained rod for bearing steel parts into a part shape in which the amount to be removed by polishing is added by hot forging, cold forging, machining, and the like. During this time, heat treatment such as normalizing or spheroidizing annealing may be performed to enhance the efficiency of forging or machining.
  • the carburizing and quenching may be performed by carbonitriding regardless of the carburizing method such as gas carburization or vacuum carburization.
  • Tempering may be performed under reduced pressure or non-oxidizing atmosphere. Machining may be performed after carburizing, quenching and tempering. And the shot peening process is implemented to the processed goods after a process. Thereafter, polishing is performed to ensure dimensional accuracy. If predetermined dimensional accuracy can be ensured after the shot peening process, the polishing step may be omitted. By manufacturing bearing steel parts in this manner, the above-described metallographic structure can be obtained.
  • the conditions in the example are an example of conditions adopted to confirm the feasibility and effects of the present disclosure, and the present disclosure describes the example of the conditions. It is not limited. The present disclosure does not deviate from the scope of the present disclosure, and various conditions can be adopted as long as the purpose of the present disclosure is achieved.
  • Shot grain Steel round cut wire ⁇ 1.0, HV 800 ⁇ Projection pressure: 0.5MPa Coverage: 400%
  • Shot grain Steel round cut wire ⁇ 1.0, HV600 ⁇ Projection pressure: 0.2MPa Coverage: 200%
  • the occurrence of peeling is detected with a vibrometer and peeling is performed with 107 times as the upper limit.
  • the lifetime was measured.
  • the Vickers hardness 50 ⁇ m deep from the rolling surface was measured as follows. Using a micro Vickers hardness tester according to JIS Z 2244: 2009, for a section obtained by cutting perpendicularly to the longitudinal direction at about 7 mm from the end face, which is the position corresponding to the test execution of the cylindrical rolling fatigue test specimen Measured. Specifically, under the conditions of a load of 200 g and a holding time of 10 seconds, the hardness of 50 ⁇ m depth from the rolling surface is measured at five points separated by 150 ⁇ m in the center distance of the depression, and arithmetically averaged Vickers hardness was determined.
  • the compressive residual stress of the rolling surface was measured as follows. It masked so that the range of 2 mm x 2 mm could be measured centering on about 7 mm position from the end surface of a cylindrical rolling fatigue test piece. Then, for the 2 mm ⁇ 2 mm range, the rolling surface is compressed using a 2 ⁇ ⁇ sin 2 ⁇ method and an Iso-Inclination method as a collimator ⁇ 1 mm using Automate (using Cr tube) manufactured by Rigaku Denki The residual stress was measured.
  • the number density of oxides having a circle equivalent diameter of 5 ⁇ m or more and a content of Al 2 O 3 of 50% by mass or more was measured as follows. It cut
  • the mass ratio of three elements other than oxygen, Ca, Al, and Si is calculated, and oxides formed by each of the three elements (that is, CaO, Al 2 O 3, and SiO 2
  • the content ratio of Al 2 O 3 is 50% by mass or more by calculating the Al 2 O 3 content with respect to the total mass of CaO, Al 2 O 3 and SiO 2 by converting it to the mass ratio of
  • the number density was calculated by dividing the number of objects by the observation area of 4 cm 2 (total observation area of 1 cm ⁇ 1 cm of observation ⁇ 4 fields of view). In the same manner, “number density of oxides having an equivalent diameter of 5 ⁇ m or more and a content of Al 2 O 3 of 50 mass% or more” of the obtained bar before forging was measured.
  • the measuring method of C content of the carburized layer of a rolling surface is demonstrated.
  • a cross section obtained by cutting perpendicularly to the longitudinal direction at a position of about 7 mm from the end face, which is a position corresponding to the test execution of the cylindrical rolling fatigue test piece using EPMA, JXA-8200 manufactured by JEOL Ltd.
  • the concentration distribution of C in the depth direction is measured at a pitch of 5 ⁇ m, and the arithmetic mean of the concentration of 50 ⁇ m from the surface on the rolling surface (that is, the position of 5 ⁇ m from the surface is the measurement start point, and the pitch of 50 ⁇ m from the surface is 5 ⁇ m)
  • the arithmetic mean of the concentration measured in (1) was taken as the C content of the carburized layer.
  • the size of the measurement point (electron beam diameter of EPMA) was ⁇ 5 ⁇ m.
  • Table 2 shows the number density of oxides having a circle equivalent diameter of 5 ⁇ m or more and a content of Al 2 O 3 of 50% by mass or more (denoted as “number density of oxides in the table”) in steel types of each sample.
  • the Vickers hardness represented as “surface hardness” in the table
  • the compressive residual stress on the rolling surface the indentation life, and the rolling fatigue life are shown.
  • the C content of the carburized layer is also shown.
  • the notation “10 ⁇ X" means “10 X ".
  • “10 ⁇ 6" means “10 6 ".
  • the underlined values in Tables 1 and 2 indicate values outside the scope of the present disclosure.
  • the blank places in the column of chemical composition in Table 1 indicate that the element corresponding to the blank places is not intentionally added.
  • No. of the disclosure example Nos. 1 to 24 have a good indentation life and rolling fatigue life while maintaining the Vickers hardness 50 ⁇ m deep from the rolling surface equal to the general bearing steel part level (Vickers hardness 750 or more).
  • Reference numeral 25 denotes SUJ 2 which is generally used, the content of chemical components, the number density of oxides having a circle equivalent diameter of 5 ⁇ m or more and the content of Al 2 O 3 of 50% by mass or more, and compression of rolling surface Since the residual stress is outside the specified range of the present disclosure and no carburizing treatment is performed, both the indentation life and the rolling fatigue life are reduced. No. of the comparative example.
  • bearing steel parts with excellent indentation life can be maintained while maintaining the surface hardness equivalent to that of general bearing steel parts if appropriate shot peening treatment is performed. Since it is obtained, it turns out that it is a steel bar suitable for obtaining the bearing steel part concerned.

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Abstract

L'invention concerne un composant d'acier de palier carburé qui a une composition chimique prédéfinie, dans laquelle : le nombre volumique d'un oxyde, qui contient CaO, Al2O3 et SiO2 et qui présente un taux de teneur en Al2O3 supérieur ou égal à 50 % en masse par rapport à la masse totale de CaO, Al2O3 et SiO2, est inférieur ou égal à 3,0/cm2 dans un diamètre circulaire équivalent supérieur ou égal à 5 µm dans une section transversale définie arbitrairement du composant; la dureté Vickers à une profondeur de 50 µm à partir de la surface de roulement est supérieure ou égale à 750; et la contrainte résiduelle de compression de la surface de roulement est supérieure ou égale à 900 MPa. L'invention concerne également une barre d'acier qui est destinée à un composant d'acier de palier carburé et qui est appropriée pour obtenir le composant d'acier de palier carburé.
PCT/JP2019/001916 2018-01-22 2019-01-22 Composant d'acier de palier carburé, et barre d'acier pour composant d'acier de palier carburé WO2019142947A1 (fr)

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