WO2017170435A1 - Acier de palier résistant à l'environnement excellent en termes de productibilité et de résistance à la fragilisation par l'hydrogène - Google Patents

Acier de palier résistant à l'environnement excellent en termes de productibilité et de résistance à la fragilisation par l'hydrogène Download PDF

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WO2017170435A1
WO2017170435A1 PCT/JP2017/012451 JP2017012451W WO2017170435A1 WO 2017170435 A1 WO2017170435 A1 WO 2017170435A1 JP 2017012451 W JP2017012451 W JP 2017012451W WO 2017170435 A1 WO2017170435 A1 WO 2017170435A1
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steel
hardness
bearing steel
hydrogen embrittlement
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PCT/JP2017/012451
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English (en)
Japanese (ja)
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木南　俊哉
良典 杉崎
工 藤田
悠 銭本
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大同特殊鋼株式会社
Ntn株式会社
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Publication of WO2017170435A1 publication Critical patent/WO2017170435A1/fr

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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
    • 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
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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

Definitions

  • the present invention relates to an environmentally resistant bearing steel that has excellent manufacturability (carburizing time and workability), suppresses a decrease in life due to hydrogen embrittlement peeling, and has a long life.
  • bearing parts such as automobiles, industrial equipment, etc., under severe load conditions such as high vibration, high load, sudden acceleration / deceleration, etc. and combined with specific lubricating oil and water mixing conditions, etc.
  • the present invention provides means for solving such problems.
  • the material strength reduction phenomenon due to hydrogen embrittlement has been known for some time.
  • diffusible hydrogen entering from the exposure environment due to decomposition of water or the like causes delayed destruction.
  • steel for springs and bolts with excellent delayed fracture resistance steel with a large amount of fine carbonitrides precipitated, trapping diffusible hydrogen, and suppressing diffusion of hydrogen to grain boundaries and stress concentration parts is used. It has been.
  • Patent Document 1 the present inventor has studied the combination of various alloy elements based on SUJ2, and as a result, by adding V, a fine V-based carbide of about several tens to several hundreds of nanometers is added. It has been found that a decrease in life due to hydrogen embrittlement under repeated fatigue conditions is suppressed.
  • Patent Document 2 by forming a Cr oxide film with Cr-added bearing steel, hydrogen penetration can be suppressed and the hydrogen embrittlement life can be extended.
  • Patent Document 3 hydrogen embrittlement is achieved by hydrogen trapping of fine nitrides such as CrN and MnSiN 2 deposited on the surface layer by carbonitriding the case-hardened steel to which Cr, Mn, etc. are added as disclosed in Patent Document 3. It is necessary to extend the service life.
  • the present invention has been made in the background as described above, and an object of the present invention is an alloy element (composition ratio of chemical components) based on bearing steel represented by SUJ2 for shortening the carbonitriding time.
  • Optimized and carbonitrided to have excellent rolling fatigue life and work such as cold forgeability and machinability even when used under atmospheric conditions where hydrogen brittle exfoliation has occurred in the past The object is to provide an environmentally resistant bearing steel having excellent properties.
  • the improvement of the hydrogen embrittlement life by carbonitriding is due to the hydrogen trap of fine nitride deposited on the surface layer.
  • the fine nitride is produced by CrN and MnSiN 2, and it is effective to increase the amount of Cr and Mn for the improvement.
  • just increasing the amount of Cr and Mn in the bearing steel increases the material hardness after spheroidizing annealing to 93HRB or higher.
  • it is effective to lower the C concentration.
  • the carbonitriding time becomes longer and the productivity is lowered.
  • Si reduction is effective in reducing hardness and increases the number of formed nitrides to improve hydrogen embrittlement resistance. This is presumably because the total number of nitrides is increased and the toughness of the mother layer is improved by changing the generated nitride from MnSiN 2 to CrN by reducing Si.
  • the inventor of the present application conducted various tests and found a component range of C amount and Si amount capable of achieving both manufacturability (carburizing time and workability) and hydrogen embrittlement resistance. Moreover, although hardenability fell by Si amount reduction, it discovered that hydrogen embrittlement resistance was improved and hardenability could be supplemented by adding Mn amount.
  • the alloy element content is expressed by mass%, C: 0.5 to 1.0%, Si: 0.1% or less, Mn: 0.4 to 1.5%, P: 0.03% or less, S: 0.03% or less, Cr: 1.5 to 3.5%, Al: 0.050% or less, O: 0.0015% or less, Ti: 0.003% or less , N: 0.015% or less, balance Fe and inevitable impurities composition, hardness after spheroidizing annealing is 92 HRB or less, surface layer N concentration after carbonitriding 0.1-1.0%, surface layer The number density of coarse CrN or MnSiN 2 nitride having a C concentration of 0.8 to 1.5%, a surface hardness of 58 to less than 64, and a particle size of 2 ⁇ m or more is 10 3 pieces / mm 2 or less, It is an environmentally resistant bearing steel excellent in manufacturability and hydrogen embrittlement resistance, characterized in that fine nitrides are dispersed and precipit
  • the bearing steel of the present invention includes V: 0.05 to 2.0%, Ni: 0.1 to 3.0%, Mo: 0.05 to 2.0%. It is preferable to further include seeds or two or more kinds. That is, the bearing steel of the present invention is expressed by mass%, C: 0.5 to 1.0%, Si: 0.1% or less, Mn: 0.4 to 1.5%, P: 0.03% S: 0.03% or less, Cr: 1.5 to 3.5%, Al: 0.050% or less, O: 0.0015% or less, Ti: 0.003% or less, N: 0.015 %: V: 0.05 to 2.0%, Ni: 0.1 to 3.0%, Mo: 0.05 to 2.0%, and further including one or more of them, The composition is preferably composed of the balance Fe and inevitable impurities.
  • an environmentally resistant bearing steel that has excellent manufacturability (carburizing time and workability), suppresses a decrease in life due to hydrogen embrittlement peeling, and has a long life.
  • the bearing steel of the present invention will be described.
  • the bearing steel of the present invention is a steel material composed of a chemical component (composition) described later, and has excellent manufacturability and hydrogen embrittlement resistance by performing at least two treatments of spheroidizing annealing and carbonitriding and quenching and tempering. Can be used as environmentally resistant bearing steel.
  • the bearing steel of the present invention is a steel material having a specific chemical composition (composition) described later, and when spheroidizing annealing is performed, the hardness immediately after that is 92 HRB or less, and carbonitriding was performed.
  • the surface layer N concentration immediately after that is 0.1 to 1.0%
  • the surface layer C concentration is 0.8 to 1.5%
  • the surface layer hardness is HRC 58 or more and less than 64
  • the grain size is 2 ⁇ m or more. If the number density of the nitride of CrN or MnSiN 2 is 10 3 pieces / mm 2 or less, the steel material after performing two treatments, spheroidizing annealing treatment and carbonitriding quenching and tempering treatment, Alternatively, it may be a steel material before performing at least one of these two treatments. Any of these corresponds to the bearing steel of the present invention.
  • C Regarding the content of C (0.5 to 1.0%), C is an essential element for securing strength as a rolling bearing. However, if the amount of C is less than 0.5%, a long time carburizing treatment is required to obtain the surface C concentration and C concentration depth distribution necessary for maintaining the strength, and the productivity is lowered. The lower limit of the amount was limited to 0.5%. However, when the C content exceeds 1.0%, the material hardness after spheroidizing annealing is increased, and it is found that workability such as cold forgeability and machinability is deteriorated. Therefore, the upper limit of the C amount is set to 1.0%.
  • Si is used as a deoxidizing agent when producing steel.
  • adding over 0.1% increases the material hardness after spheroidizing annealing, lowers the machinability and cold forgeability, and the nitride form after carbonitriding changes from CrN to MnSiN 2
  • the upper limit is set to 0.1%.
  • Mn is an element used for deoxidation when manufacturing steel.
  • Mn is an element that improves hardenability, and complements the decrease in hardenability due to the suppression of the amount of C and Si for cold forgeability and machinability, and MnSiN that becomes a hydrogen trap site after carbonitriding
  • the hydrogen embrittlement resistance can be improved by finely increasing 2 to precipitate 2.
  • an Mn amount of 0.4% or more is required, so the lower limit of Mn is 0.4%. did.
  • Mn is contained in a large amount exceeding 1.5%, the material hardness after spheroidizing annealing is increased and the machinability and cold forgeability are lowered, so the upper limit of Mn content is 1.5%. Limited to.
  • S content (0.03% or less)
  • S impairs hot workability of steel and forms non-metallic inclusions in the steel to reduce toughness and rolling life. Although it is desirable to reduce it, since S also has the effect of improving the machinability, 0.03% was made the upper limit of S.
  • Cr is added to improve hardenability, ensure hardness by carbides and improve life. Furthermore, by depositing CrN after carbonitriding, it becomes a hydrogen trap site and can improve hydrogen embrittlement resistance. In order to obtain this effect, addition of 1.5% or more is necessary, so the lower limit value of the Cr content is limited to 1.5%. However, if the content exceeds 3.5%, the material hardness after spheroidizing annealing is increased, and the machinability and cold forgeability are reduced, and a large carbonitride is formed, which has a rolling fatigue life. Since the reduction occurs, the upper limit of the Cr content is set to 3.5%.
  • Al content (0.050% or less)
  • Al is used as a deoxidizer during steel production, but it is reduced to produce hard non-metallic inclusions and reduce rolling fatigue life. Is desirable.
  • the upper limit of the Al content is set to 0.050%.
  • the lower limit of the Al content is preferably set to 0.005%.
  • Ti content (0.003% or less), O (oxygen) content (0.0015% or less), and N content (0.015% or less)
  • Ti, O and N are oxidized in steel.
  • Ti, 0.003%, O: 0.0015%, and N: 0.015% are included in each element in order to reduce fatigue life as non-metallic inclusions by forming oxides and nitrides. The upper limit.
  • V content (0.05 to 2.0%), V precipitates fine V-based carbides with a particle size of several hundred nanometers or less, and suppresses hydrogen embrittlement delamination by trapping diffusible hydrogen in steel. There is an effect to.
  • the V content is preferably 0.05% or more.
  • the upper limit of the V content is preferably 2.0%.
  • Ni suppresses the structural change during the rolling fatigue process and improves the rolling fatigue life. Further, the addition of Ni is effective in improving toughness and corrosion resistance. In order to obtain these effects, the Ni content is preferably 0.1% or more. However, if it is contained in a large amount exceeding 3.0%, a large amount of retained austenite is generated at the time of quenching the steel, and the predetermined hardness cannot be obtained, and the cost of the steel material may increase, so the Ni content Is preferably 3.0%.
  • Mo has the effect of improving the hardenability of the steel and suppressing the decrease in hardness during tempering by dissolving in the carbide.
  • the Mo content is preferably 0.05% or more.
  • the upper limit value of Mo is preferably 2.0%. .
  • the bearing steel of the present invention is a steel material containing C, Si, Mn, P, S, Cr, Al, O, Ti, and N at a specific ratio, and one or more of V, Ni, and Mo It is preferable that it contains 2 or more types, and the balance may be Fe and inevitable impurities.
  • inevitable impurities that can be contained in Fe include conventionally known components. For example, Cu etc. are mentioned. The smaller the content of inevitable impurities, the better.
  • nitrides effective for hydrogen trapping are fine Cr nitrides (eg, CrN) having a particle size of 300 nm or less, and composite nitrides of Mn and Si (eg, MnSiN 2 ).
  • nitrides effective for hydrogen trapping are fine Cr nitrides (eg, CrN) having a particle size of 300 nm or less, and composite nitrides of Mn and Si (eg, MnSiN 2 ).
  • increasing the surface layer N concentration and the alloy element facilitates the formation of coarse nitrides having a large particle size, which causes a decrease in strength.
  • the number ratio of coarse CrN or MnSiN 2 nitride having a particle size of 2 ⁇ m or more exceeds 10 3 pieces / mm 2 , the hydrogen embrittlement type surface fatigue strength is significantly reduced.
  • the upper limit of the number ratio was 10 3 pieces / mm 2 .
  • a method for measuring the number of coarse CrN or MnSiN 2 nitride having a particle diameter of 2 ⁇ m or more will be described later.
  • the surface layer C is an essential element for securing the strength as a rolling bearing, and the surface layer C concentration of 0.8% or more is necessary to maintain the hardness after a predetermined heat treatment.
  • the lower limit was defined as 0.80%.
  • the upper limit of the surface layer C concentration was 1.5%.
  • concentration is mentioned later.
  • the surface layer N works as a hydrogen trap site by generating fine nitride in the surface layer, and improves hydrogen embrittlement resistance. It also improves the rolling life by improving the softening resistance of the steel.
  • the surface layer N concentration needs to be 0.1% or more, so the lower limit of the surface layer N concentration was set to 0.1%.
  • the upper limit of the surface layer N concentration is set to 1.0%. A method for measuring the surface layer N concentration will be described later.
  • the method for producing the bearing steel of the present invention is not particularly limited.
  • the bearing steel of the present invention can be obtained by adjusting the raw materials so as to contain the specific chemical component (composition) as described above, and dissolving and solidifying by a conventionally known method.
  • the raw material is adjusted so that the bearing steel of the present invention contains the specific chemical component (composition) as described above, melted and solidified by a conventionally known method, and then rolled and subjected to spheroidizing annealing treatment.
  • the rolling is preferably hot rolling and low temperature rolling.
  • the spheroidizing annealing treatment includes heating to 700 to 800 ° C., holding for 1 to 10 hours, cooling to 450 to 700 ° C. at ⁇ 5 to ⁇ 30 ° C./hour, and then air cooling. Is done.
  • the carbonitriding quenching and tempering process is exemplified by the process shown in FIG.
  • the spheroidizing annealing hardness is a hardness test piece in which the cross section of the spheroidizing annealing material having a diameter of 32 mm (surface perpendicular to the longitudinal axis of the steel bar) is exposed, and is 1 ⁇ 2 of the cross section
  • the HRB hardness JIS Z2245
  • the measurement results are shown in the column of “spheroidizing annealing hardness (HRB)” in Table 2.
  • FIG. 1 is an example of the carbonitriding conditions used. In Table 1, No. 5 and no. As for the steel No.
  • the test piece obtained by performing the carbonitriding quenching and tempering treatment as described above was ground at a depth of 0.15 mm, and the Rockwell hardness (conforming to JIS Z2245) was determined for the outer peripheral portion with an average of 5 points. The results are shown in the column of “surface hardness (HRC)” in Table 2.
  • the test piece obtained by performing the carbonitriding quenching and tempering treatment as described above was embedded in the resin so that the cross section (surface perpendicular to the longitudinal axis of the steel bar) was exposed, and the cross section was polished and finished.
  • the C and N concentrations in the surface layer were analyzed by EPMA. The results are shown in the columns of “surface layer C concentration” and “surface layer N concentration” in Table 2. Here, the surface layer C and N concentrations were the maximum values (peak values) of the C and N concentrations from the outermost layer to a depth of 10 ⁇ m.
  • the number of nitrides having a particle diameter of 2 ⁇ m or more existing in the depth region from the surface layer to a depth of 100 ⁇ m was measured using FE-SEM and elemental analysis (EDX).
  • the number density (pieces / mm 2 ) of coarse nitrides having a particle size of 2 ⁇ m or more was determined. The results are shown in Table 2.
  • a mating cylinder 20 made of a tempered tempering material of JIS SUJ2 is pressed against the test piece 18 with a predetermined surface pressure.
  • the test piece 18 was rotated through 24 and the rotation of the motor 22 was transmitted to the shaft 30 through the gears 26 and 28 to rotate the counterpart cylinder 20.
  • the counterpart cylinder is a SUJ2 quenching and tempering material, and the shape is a cylinder with a diameter of 130 mm having a crowning with a curvature radius of 150 mm in the axial direction.
  • the test conditions were such that the hydrogen embrittlement type surface fatigue peeling was reproduced.
  • the test was performed under the test conditions (oil temperature 90 ° C., slip rate ⁇ 60%, surface pressure 3 Gpa, rotation speed 1500 rpm) in which a hydrogen embrittlement type lubricating oil was used and an early rolling fatigue failure of the hydrogen embrittlement type occurred.
  • the slip ratio is a ratio of the difference between the peripheral speeds of the test cylinder and the counterpart cylinder and the peripheral speed of the test cylinder.
  • the test was performed at four points under the same conditions, and the average life was obtained. Table 2 shows the test results.
  • the steels of the present invention corresponding to the present invention each have a surface hardness (HRC) of 58 or more and less than 64, the surface layer C content in the range of 0.8 to 1.5%, and the surface layer N content. Is in the range of 0.1 to 1.0%, and the number of coarse nitrides having a particle size of 2 ⁇ m or more is 10 3 pieces / mm 2 or less. Further, the average life of the two-cylinder test of the steel of the present invention is excellent at 10.6 to 19.3 ⁇ 10 6 times. On the other hand, in the comparative steel, the steel type No. The average lifespans of 13, 15, 1, and 2 are 0.5 to 4.7 ⁇ 10 6 times, which are all low due to hydrogen embrittlement.
  • HRC surface hardness
  • steel type No. in the comparative steel. Nos. 1 and 2 have the chemical composition No. Although it is the same as 1 and 2, it is an example in which the surface layer C, N concentration or surface layer hardness after carbonitriding is out of the range.
  • steel type No. Nos. 14 and 16 have a long life of 10.4 to 12.1 ⁇ 10 6 times, but the material hardness after spheroidizing annealing is as high as 93,94 HRB and is inferior in manufacturability.
  • the steel type No. No. 13 is an example in which Si is a high chemical component and coarse nitrides are produced, resulting in a short life. No. No.
  • No. 14 is an example in which the material hardness is increased due to the high amount of C.
  • No. No. 15 is an example in which the lifetime is reduced due to the low amount of Mn.
  • No. 16 is an example in which the Cr content is high and the material hardness is high.
  • steel type No. in the examples using Nos. 1 and 2 the chemical composition is the steel type No. in the steel of the present invention. Although it is the same as 1 and 2, it is an example in which the lifetime is reduced for the following reason.
  • Steel type no. No. 2 is an example in which nitriding is not performed and the surface layer N concentration is low, resulting in a short life.
  • an environmentally resistant bearing steel that has excellent manufacturability (carburizing time and workability), suppresses a decrease in life due to hydrogen embrittlement peeling, and has a long life.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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Abstract

La présente invention concerne un acier de palier résistant à l'environnement excellent en termes de productibilité et de résistance à la fragilisation par l'hydrogène, l'acier de palier étant caractérisé en ce qu'il présente une composition qui comporte, en pourcentages massiques, de 0,5 à 1,0 % de C, jusqu'à 0,1 % de Si, de 0,4 à 1,5 % de Mn, jusqu'à 0,03 % de P, jusqu'à 0,03 % de S, de 1,5 à 3,5 % de Cr, jusqu'à 0,050 % d'Al, jusqu'à 0,0015 % d'O, jusqu'à 0,003 % de Ti et jusqu'à 0,015 % de N, le reste comprenant du Fe et des impuretés inévitables. L'acier de palier est en outre caractérisé en ce qu'après un recuit de sphéroïdisation, l'acier présente une dureté de 92 HRB ou moins et qu'après une carbonitruration, l'acier présente une concentration en azote dans la couche de surface de 0,1 à 1,0 %, une concentration en carbone dans la couche de surface de 0,8 à 1,5 %, et une dureté de couche de surface de 58 ou plus mais inférieure à 64 en termes de HRC, la densité en nombre de grains de nitrure grossiers de CrN ou de MnSiN2 qui présentent des diamètres de grain de 2 µm ou plus étant inférieure ou égale à 103 grains/mm2. L'acier de palier est caractérisé en ce que des grains de nitrure fins ont été dispersés et précipités.
PCT/JP2017/012451 2016-03-30 2017-03-27 Acier de palier résistant à l'environnement excellent en termes de productibilité et de résistance à la fragilisation par l'hydrogène WO2017170435A1 (fr)

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JP2016069716A JP6735589B2 (ja) 2016-03-30 2016-03-30 製造性と耐水素脆性に優れた耐環境用軸受鋼

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CN111100973A (zh) * 2019-12-28 2020-05-05 临清市东华轴承钢管有限责任公司 一种轴承钢管快速球化退火工艺
WO2025027670A1 (fr) * 2023-07-28 2025-02-06 株式会社ジェイテクト Composant de piste de palier et procédé de fabrication d'un composant de piste de palier

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2013234702A (ja) * 2012-05-08 2013-11-21 Nsk Ltd プラネタリギヤ装置
JP2014012870A (ja) * 2012-07-04 2014-01-23 Daido Steel Co Ltd 水素脆性型の面疲労強度に優れた浸炭窒化部品
JP2014152378A (ja) * 2013-02-13 2014-08-25 Ntn Corp 軸受部品
JP2014185379A (ja) * 2013-03-25 2014-10-02 Nachi Fujikoshi Corp 水素脆性型の面疲労強度に優れた浸炭窒化軸受部品
JP2014189895A (ja) * 2013-03-28 2014-10-06 Kobe Steel Ltd 転動疲労特性に優れた肌焼鋼
JP2015094021A (ja) * 2013-11-14 2015-05-18 大同特殊鋼株式会社 水素脆性型の面疲労強度に優れた浸炭窒化鋼及びそれを用いた浸炭窒化部品

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2013234702A (ja) * 2012-05-08 2013-11-21 Nsk Ltd プラネタリギヤ装置
JP2014012870A (ja) * 2012-07-04 2014-01-23 Daido Steel Co Ltd 水素脆性型の面疲労強度に優れた浸炭窒化部品
JP2014152378A (ja) * 2013-02-13 2014-08-25 Ntn Corp 軸受部品
JP2014185379A (ja) * 2013-03-25 2014-10-02 Nachi Fujikoshi Corp 水素脆性型の面疲労強度に優れた浸炭窒化軸受部品
JP2014189895A (ja) * 2013-03-28 2014-10-06 Kobe Steel Ltd 転動疲労特性に優れた肌焼鋼
JP2015094021A (ja) * 2013-11-14 2015-05-18 大同特殊鋼株式会社 水素脆性型の面疲労強度に優れた浸炭窒化鋼及びそれを用いた浸炭窒化部品

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