WO2023080029A1 - Matériau d'acier pour composants coulissants et procédé de production de matériau d'acier pour composants coulissants - Google Patents

Matériau d'acier pour composants coulissants et procédé de production de matériau d'acier pour composants coulissants Download PDF

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WO2023080029A1
WO2023080029A1 PCT/JP2022/039894 JP2022039894W WO2023080029A1 WO 2023080029 A1 WO2023080029 A1 WO 2023080029A1 JP 2022039894 W JP2022039894 W JP 2022039894W WO 2023080029 A1 WO2023080029 A1 WO 2023080029A1
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steel material
sliding parts
iron carbide
less
volume fraction
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PCT/JP2022/039894
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English (en)
Japanese (ja)
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なつみ 菊地
基成 西原
達彦 安部
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日本製鉄株式会社
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Priority to JP2023557972A priority Critical patent/JPWO2023080029A1/ja
Priority to CN202280073772.0A priority patent/CN118202078A/zh
Publication of WO2023080029A1 publication Critical patent/WO2023080029A1/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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/30—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for crankshafts; for camshafts
    • 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
    • C22C38/60—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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  • the present invention relates to a steel material for sliding parts and a method for manufacturing the steel material for sliding parts.
  • Steel materials are widely used in industrial products such as automotive parts, railway vehicle parts, building components, and pipes.
  • carbon steel materials for machine structural use and alloy steel materials for machine structural use are often used as materials for sliding parts such as gears and shafts, typified by power transmission system parts, because of their high mechanical strength.
  • One of the issues to be solved for steel materials for sliding parts is to improve wear resistance from the viewpoint of extending the life of parts and improving reliability. It is considered effective to increase the hardness of steel materials to improve wear resistance. However, increasing the hardness impairs the machinability of the steel material, which entails risks when mass-producing parts. Therefore, as a method for improving the slidability of sliding parts, it is effective to selectively control the structure of only the surface layer and harden only the relevant portion.
  • Japanese Patent Application Laid-Open No. 1-230746 discloses a sliding component comprising a fixed member made of cast iron and a sliding member made of a material having higher hardness than cast iron, wherein the surface layer structure of the fixed member is martensite or martensite. It is disclosed that the hardened layer consists of a mixed phase structure of , pearlite, ferrite and graphite, and the structure consists of oxides.
  • tempered martensite and/or tempered bainite contain retained austenite at an area ratio of 1 to 10%, and carbide precipitates at an area ratio of 5% or more. It describes a gear having a steel material structure with a high nitrogen content and a nitrogen concentration of 2.0 to 6.0% at a depth of 20 ⁇ m from the surface.
  • Japanese Patent Application Laid-Open No. 2010-100881 describes a carburized or carbonitrided sliding part, in which a surface layer portion up to a depth of 10 ⁇ m from the surface of the sliding surface has Vickers at a depth of 10 ⁇ m from the surface of the sliding surface.
  • a sliding part having a hardness of 700 or more, an average particle diameter of cementite particles of 0.6 ⁇ m or less, and a number density of cementite particles in a cross section perpendicular to the sliding surface of 1 piece/ ⁇ m 2 or more is described. ing.
  • An object of the present invention is to provide a steel material for sliding parts that has excellent slidability and workability. Another object of the present invention is to provide a method for producing a steel material for sliding parts that is excellent in slidability and workability.
  • a steel material for sliding parts is a steel material for sliding parts comprising a steel material having a C content of 0.30 to 0.60% by mass, and having a structure of tempered martensite and bainite. At least one of them and iron carbide, the total volume fraction of the tempered martensite and the bainite is 80% or more, the iron carbide is 2.0% or more, and the Vickers hardness is 300 or more and 600 or less and the volume fraction X of the iron carbide and the Vickers hardness Hv satisfy the following relational expression (1).
  • X ⁇ 0.065 ⁇ Hv+36.5 (1)
  • the unit of X is % and the unit of Hv is Hv.
  • a steel material for sliding parts according to an embodiment of the present invention has a chemical composition, in mass %, of C: 0.30 to 0.60%, Si: 0.01 to 2.00%, Mn: 0.00%. 10 to 2.00%, Al: 0.060% or less, N: 0.020% or less, P: 0.10% or less, S: 0.20% or less, Cr: 0 to 0.50%, balance: It may be Fe and impurities.
  • a method for producing a steel material for sliding parts is a method for producing the above-mentioned steel material for sliding parts, wherein after holding the material at a temperature of 830° C. or more and 1100° C. or less, from the holding temperature A step of cooling and quenching so that the cooling rate to 300° C. is 300° C./sec or more, and a step of holding the quenched material at a temperature of 200° C. or more and 600° C. or less and tempering it.
  • FIG. 1 is an uneven image of a steel material acquired by an atomic force microscope.
  • FIG. 2 is an adhesion force image of steel obtained by an atomic force microscope.
  • FIG. 3 is a scatter diagram showing the relationship between the Vickers hardness of steel and the volume fraction of iron carbide.
  • FIG. 4 is a graph showing the relationship between the Vickers hardness of steel and the wear scar width obtained by a sliding test using a ball-on-disk type friction wear tester.
  • FIG. 5 is an example of an uneven image obtained by measuring a test piece whose surface has been processed by Ar ion milling with an atomic force microscope.
  • FIG. 6 is an example of iron carbide detected by image analysis software.
  • FIG. 7 is a schematic diagram of a ball-on-disk type friction and wear tester.
  • the inventors investigated the slidability and workability of steel materials in order to develop steel materials with excellent slidability and workability. As a result, the following findings were obtained.
  • Figures 1 and 2 are images obtained by an atomic force microscope (AFM), where Figure 1 is an uneven image and Figure 2 is an adhesive force image.
  • AFM atomic force microscope
  • FIG. 1 the convex portions are shown in white, and the concave portions are shown in black.
  • FIG. 2 portions with high adhesive strength are displayed in white, and portions with low adhesive strength are displayed in black.
  • FIG. 1 The uneven image in Fig. 1 was obtained by AFM measurement of a sample whose surface was processed by Ar ion milling. As a result of this processing, the iron matrix, which is softer than the iron carbide, is scraped away, leaving the iron carbide as a convex, which makes it possible to search for the iron carbide by AFM.
  • white portions, that is, convex portions are iron carbides.
  • FIG. 2 shows the result of measuring the adhesion force in the same range, and it can be seen from FIGS. 1 and 2 that the adhesion force of iron carbide is small.
  • the seizure resistance can be improved by increasing the volume fraction of iron carbide.
  • the volume fraction of iron carbide is increased, the hardness of the steel material may be lowered and the wear resistance may be lowered.
  • FIG. 3 is a scatter diagram showing the relationship between the Vickers hardness of steel materials produced in Examples described later and the volume fraction of iron carbide.
  • FIG. 4 is a graph showing the relationship between the Vickers hardness of steel and the wear scar width obtained by a sliding test using a ball-on-disk type friction wear tester. The smaller the wear scar width, the higher the wear resistance.
  • the volume fraction X of the iron carbide and the Vickers hardness Hv of the steel satisfy the following relational expression (1). are indicated by solid circle symbols. Note that the triangular symbols in FIG. 4 are for steel materials with an as-quenched structure. X ⁇ 0.065 ⁇ Hv+36.5 (1) The unit of X is % and the unit of Hv is Hv.
  • the steel material for sliding parts according to this embodiment is made of a steel material having a C content of 0.30 to 0.60% by mass.
  • the lower limit of the C content of the steel material for sliding parts according to the present embodiment is preferably 0.32% by mass, more preferably 0.35% by mass, still more preferably 0.38% by mass, and Preferably it is 0.40% by mass.
  • the upper limit of the C content of the steel material for sliding parts according to the present embodiment is preferably 0.58% by mass, more preferably 0.55% by mass.
  • the chemical composition of the steel material for sliding parts according to the present embodiment is not particularly limited as long as the C content is 0.30 to 0.60% by mass. may In the following description, "%" of element content means % by mass.
  • C 0.30-0.60% Carbon (C) enhances the hardenability of steel. As described above, if the C content is out of the appropriate range, it becomes difficult to satisfy the relational expression (1) between the volume fraction of iron carbide and the Vickers hardness, or even if the relational expression (1) is satisfied, In some cases, it may not be possible to obtain a steel material with an excellent balance between dynamicity and workability. Therefore, the C content is 0.30-0.60%.
  • the lower limit of the C content is preferably 0.32%, more preferably 0.35%, still more preferably 0.38%, still more preferably 0.40%.
  • the upper limit of the C content is preferably 0.58%, more preferably 0.55%.
  • Si 0.01-2.00% Silicon (Si) deoxidizes steel. On the other hand, if the Si content is too high, the workability of the steel deteriorates. Therefore, the Si content may be 0.01-2.00%.
  • the lower limit of the Si content is preferably 0.02%, more preferably 0.05%, still more preferably 0.10%.
  • the upper limit of the Si content is preferably 1.50%, more preferably 1.20%, still more preferably 0.80%, still more preferably 0.60%, still more preferably 0 .40%.
  • Mn 0.10-2.00%
  • Mn Manganese
  • the lower limit of the Mn content is preferably 0.20%, more preferably 0.40%, still more preferably 0.60%.
  • the upper limit of the Mn content is preferably 1.80%, more preferably 1.60%, still more preferably 1.50%, still more preferably 1.00%, still more preferably 0 .90%.
  • Al 0.060% or less Aluminum (Al) deoxidizes steel. On the other hand, if the Al content is too high, the workability of the steel deteriorates. Therefore, the Al content may be 0.060% or less.
  • the upper limit of the Al content is preferably 0.050%, more preferably 0.040%, still more preferably 0.030%. When obtaining the deoxidizing effect of Al, the Al content may be 0.020% or more.
  • N 0.020% or less Nitrogen (N) reduces the hot workability of steel. Therefore, the N content may be 0.020% or less.
  • the upper limit of the N content is preferably 0.018%, more preferably 0.015%, still more preferably 0.010%, still more preferably 0.005%.
  • the lower limit of the N content may be 0.0010%.
  • P 0.10% or less Phosphorus (P) is an impurity. P segregates at grain boundaries and lowers the hot workability and toughness of steel. Therefore, the P content may be 0.10% or less.
  • the P content is preferably 0.03% or less, more preferably 0.02% or less. It is preferable that the P content is as low as possible.
  • S 0.20% or less Sulfur (S) is sometimes added to improve the workability (machinability) of steel.
  • the S content may be 0.20% or less.
  • the upper limit of the S content is preferably 0.12%, more preferably 0.08%, still more preferably 0.06%.
  • the S content may be 0.020% or more.
  • Chromium (Cr) is an optional element. That is, the steel material for sliding parts according to this embodiment does not have to contain Cr. Cr increases the hardenability of steel. This effect can be obtained if even a small amount of Cr is contained. On the other hand, if the Cr content is too high, the workability of the steel deteriorates. Therefore, the Cr content may be 0-0.50%.
  • the lower limit of the Cr content is preferably 0.01%, more preferably 0.05%.
  • the upper limit of Cr content is preferably 0.20%.
  • the rest of the chemical composition of the steel material for sliding parts according to this embodiment may be Fe and impurities.
  • impurities refers to elements mixed in from ores and scraps used as raw materials for steel, or elements mixed in from the environment during the manufacturing process.
  • the steel material for sliding parts according to this embodiment may consist of a carbon steel material for machine structural use or an alloy steel material for machine structural use.
  • the steel material for sliding parts according to this embodiment preferably consists of a carbon steel material for machine structural use specified in JIS G 4051:2016 or an alloy steel material for machine structural use specified in JIS G 4053:2016.
  • S45C and S50C of JIS G 4051:2016 and SMn438 of JIS G 4053:2016 are particularly preferable.
  • these steel materials may contain 0.20% by mass or less of S in order to improve workability (machinability).
  • the structure of the steel material for sliding parts includes at least one of tempered martensite and bainite (including tempered bainite; the same applies hereinafter) and iron carbide, and the volume fraction of tempered martensite and Total with bainite: 80% or more, iron carbide: 2.0% or more.
  • the sum of the volume fraction of tempered martensite and the volume fraction of bainite is 80% or more.
  • the structure of the steel material for sliding parts according to the present embodiment may contain at least one of tempered martensite and bainite.
  • the steel material for sliding parts is tempered to obtain a structure containing a predetermined amount of iron carbide, thereby ensuring workability of the steel material for sliding parts.
  • the structure of the steel material for sliding parts is as quenched (structure mainly composed of martensite as quenched), it becomes difficult to ensure good workability.
  • the steel material for sliding parts according to the present embodiment preferably contains tempered martensite.
  • the sum of the volume fraction of tempered martensite and the volume fraction of bainite is preferably 85% or more, more preferably 90% or more, and still more preferably 95% or more.
  • iron carbide in calculating the volume fraction of the structure, is treated as an independent structure and iron carbide is distinguished from tempered martensite and bainite. That is, the portion where iron carbide precipitates is not included in the volume of tempered martensite or bainite.
  • the structure of the steel material for sliding parts according to this embodiment has a volume fraction of iron carbide of 2.0% or more.
  • the iron carbide of the steel material for sliding parts according to the present embodiment is at least one of ⁇ carbide and cementite.
  • the iron carbide contained in the steel material for sliding parts may be of one type or of a plurality of types. When multiple types of iron carbide are included, the volume fraction of iron carbide is the sum of the volume fractions of those iron carbides.
  • the lower limit of the volume fraction of iron carbide is preferably 3.0%, more preferably 5.0%, still more preferably 7.0%.
  • the upper limit of the volume fraction of iron carbide is preferably 18.0%, more preferably 15.0%, still more preferably 12.0%, still more preferably 10.0%, and Preferably it is 8.0%.
  • the volume fraction of iron carbide can be adjusted by the C content of the steel material and the tempering conditions. Specifically, the higher the C content, the higher the volume fraction of iron carbide. As for tempering conditions, the higher the holding temperature and the longer the holding time, the higher the volume fraction of iron carbide.
  • the structure of the steel material for sliding parts according to this embodiment may contain a small amount of structure other than tempered martensite, bainite, and iron carbide.
  • Structures other than tempered martensite, bainite, and iron carbide are, for example, ferrite, pearlite, retained austenite, MnS, and the like.
  • the total volume fraction of structures other than tempered martensite, bainite, and carbide in the structure of the steel material for sliding parts according to the present embodiment is preferably 5.0% or less, more preferably 3.0% or less. , more preferably 2.0% or less, and still more preferably 1.0% or less.
  • the steel material for sliding parts according to this embodiment has a Vickers hardness of 300 or more and 600 or less. If the Vickers hardness is less than 300, it becomes difficult to obtain excellent wear resistance. On the other hand, when the Vickers hardness is higher than 600, workability is lowered. From the viewpoint of wear resistance, the lower limit of the Vickers hardness is preferably 350, more preferably 400, still more preferably 450, more preferably 500, still more preferably 530. From the viewpoint of workability, the upper limit of the Vickers hardness is preferably 580, more preferably 560, still more preferably 550, still more preferably 530, still more preferably 520.
  • the Vickers hardness of the steel material for sliding parts can be adjusted by the C content of the steel material, the quenching conditions, and the tempering conditions. Specifically, the higher the C content, the higher the Vickers hardness tends to be. As for the quenching conditions, the higher the cooling rate, the higher the Vickers hardness tends to be. As for the tempering conditions, the lower the holding temperature and the shorter the holding time, the higher the Vickers hardness tends to be.
  • the average minor axis length of the iron carbide is preferably 0.027 ⁇ m or less.
  • the average minor axis length of the iron carbide is preferably 0.025 ⁇ m or less.
  • the steel material for sliding parts according to this embodiment preferably has no nitrided layer, carburized layer, or carbonitrided layer on the surface.
  • the steel material for sliding parts according to the present embodiment has a surface Vickers hardness of 300 or more and 600 or less, and the volume fraction X of iron carbide on the surface and the Vickers hardness Hv satisfy the above-described relational expression (1). is preferred.
  • the "surface Vickers hardness” more specifically means the Vickers hardness of a region at a depth of 100 ⁇ m or less from the surface of the steel material for sliding parts.
  • the volume fraction of iron carbide on the surface more specifically means the volume fraction of iron carbide in the structure of the region at a depth of 100 ⁇ m or less from the surface of the steel material for sliding parts.
  • the material is, for example, a hot forged product.
  • the steel having the above-described chemical composition is melted, continuous casting or blooming rolling is performed to make a steel slab, and the steel slab is hot forged and processed into a rough shape for sliding parts.
  • can be Cutting or the like may be applied to the material after hot forging.
  • the material After holding the material at a temperature of 830°C or higher and 1100°C or lower, it is cooled and quenched so that the cooling rate from the holding temperature to 300°C is 300°C/second or more. If the holding temperature is too low, a uniform texture may not be obtained. On the other hand, if the holding temperature is too high, the crystal grains may become coarse. If the cooling rate is too low, the desired structure may not be obtained. Note that the Vickers hardness of the finally obtained steel material for sliding parts tends to increase as the cooling rate in the quenching process increases.
  • the quenched material is tempered while being held at a temperature of 200°C or higher and 600°C or lower.
  • the higher the holding temperature and the longer the holding time of tempering the lower the Vickers hardness of the finally obtained steel material for sliding parts.
  • the higher the holding temperature and the longer the holding time of tempering the higher the volume fraction of iron carbide in the structure of the finally obtained steel material for sliding parts. If the holding temperature for tempering is out of this range, it becomes difficult to keep the volume fraction of iron carbide and the Vickers hardness within the predetermined ranges.
  • the conditions for quenching and tempering are adjusted according to the chemical composition of the steel material, so that the volume fraction X of iron carbide and the Vickers hardness Hv satisfy the relational expression (1). As a result, the steel material for sliding parts according to the present embodiment is obtained.
  • the steel material for sliding parts according to one embodiment of the present invention has been described above.
  • the steel material for sliding parts according to this embodiment has excellent slidability and workability. Therefore, the steel material for sliding parts according to this embodiment is suitable as a material for sliding parts.
  • a sliding part is, for example, a crankshaft.
  • a 10 kg steel having the chemical composition shown in Table 1 was melted in a vacuum induction melting furnace to produce an ingot.
  • This ingot was hot forged at 950-1200°C to a thickness of 30 mm, a width of 100 mm and a length of 290 mm, and then rolled to a thickness of 7 mm and a width of 110 mm.
  • the rolled material was cut into pieces having a width of 15 mm, a length of 60-120 mm, and a thickness of 7 mm, and subjected to the heat treatment shown in Table 2.
  • the structures before the heat treatment were all ferrite/pearlite (F+P).
  • the numerical values in the "cooling rate" column of "quenching" in Table 2 are the cooling rates from the holding temperature of quenching to 300°C.
  • test pieces After the heat treatment, multiple 20 mm square and 2 mm thick test pieces were taken from each material. Observation of the structure, measurement of Vickers hardness, and evaluation of slidability were performed using these test pieces.
  • FIG. 5 shows an example of a surface unevenness image of a processed test piece obtained by AFM.
  • White indicates convex portions, and black indicates concave portions.
  • White portions in FIG. 5 are iron carbides.
  • the volume fraction of iron carbide was calculated using image analysis software after acquiring uneven images in the range of 2 ⁇ m ⁇ 2 ⁇ m by AFM at three locations on the test piece.
  • ImageJ was used as image analysis software.
  • the image was binarized and the particles were detected using the particle analysis function of the image analysis software.
  • An example of iron carbide detected by image analysis software is shown in FIG.
  • the area ratio of iron carbide was calculated at each of the three observed locations, and the average was obtained. The obtained area ratio was regarded as the volume fraction of iron carbide.
  • the volume fraction of ferrite was calculated using a secondary electron image (unevenness image) of SEM.
  • the surface of the sample was nital-etched to corrode only the ferrite to form a recess, and then a secondary electron image was obtained at a magnification of 1000 times.
  • the acquired image is imported into the image analysis software ImageJ, the relevant area is selected using the freehand selection or polygon selection function, the selected area is masked, binarization is performed in the same way as for iron carbide, and the particles of the image analysis software The relevant regions were detected using the analysis function.
  • the area ratio of ferrite was calculated at each of the three observed points, and the average was obtained. The obtained area ratio was regarded as the volume fraction of ferrite.
  • the volume fraction of retained austenite was measured by X-ray diffraction.
  • the volume fraction of MnS was obtained by photographing the surface of the test piece with an optical microscope (magnification: 210 times, size of field of view: 1218 ⁇ m ⁇ 1218 ⁇ m) to determine the area ratio of MnS, and this area ratio was regarded as the volume fraction. .
  • the sum of the volume fraction of tempered martensite and the volume fraction of bainite is the volume fraction of iron carbide, retained austenite, ferrite, and MnS. It was obtained by subtracting the sum of from 100%.
  • the morphology of the iron carbide was determined by image analysis from the uneven image obtained when determining the volume fraction of the iron carbide. Specifically, the images were binarized, and all particles within each observation field were elliptically approximated using the particle analysis function of the image analysis software. An average minor axis length and an average major axis length were obtained at each of the three observed points, and the average thereof was obtained.
  • the Vickers hardness was measured at 5 points with a test force of 1 kgf (9.807 N), and the average was obtained.
  • Table 3 shows the structure and Vickers hardness of each steel material after heat treatment.
  • M represents as-quenched martensite
  • B represents bainite
  • TM represents tempered martensite
  • restored ⁇ represents retained austenite.
  • the surface of the specimen for the sliding test was mirror-finished.
  • the sliding test was performed using a ball-on-disk type friction wear tester.
  • FIG. 7 shows a schematic diagram of the test machine. Alumina balls were used, the load was 10 N, and the sliding speed was 10 mm/sec. After the sliding test, the width of the sliding marks was measured, and if the average value of the sliding mark width was 160 ⁇ m or less, the wear resistance was evaluated as “good”, and if it exceeded 160 ⁇ m, the wear resistance was poor. It was rated as "impossible”.
  • Table 4 shows the Vickers hardness of each steel material, the volume fraction of carbides (iron carbides), and the results of the sliding test. The workability was evaluated as “good” if the Vickers hardness was 600 or less, and as “poor” if it exceeded 600. In the comprehensive evaluation, samples with “good” workability and wear resistance were rated as “acceptable”, and samples with either “poor” workability or wear resistance were rated as “fail”.
  • the steel materials of 4 to 7, 9, 10 and 14 to 17 have a Vickers hardness of 300 to 600, and the volume fraction X of iron carbide and the Vickers hardness Hv satisfy the relational expression (1). These test materials had a wear scar width of 160 ⁇ m or less after the sliding test, indicating excellent wear resistance. Moreover, these test materials had a Vickers hardness Hv of 600 or less and were excellent in workability.
  • the steel material No. 11 has the structure as quenched. No. The steel material No. 11 had good wear resistance, but had a Vickers hardness Hv exceeding 600 and was inferior in workability.
  • FIG. 3 is a scatter diagram showing the relationship between the Vickers hardness of steel and the volume fraction of iron carbide.
  • FIG. 4 is a graph showing the relationship between the Vickers hardness of steel and the wear scar width obtained by a sliding test using a ball-on-disk type friction wear test. 3 and 4, the volume fraction X of the iron carbide and the Vickers hardness Hv of the steel material satisfy the relational expression (1) by the white circle symbol, and the relational expression (1) is satisfied. Those that are not are indicated by a solid circle symbol.
  • the triangular symbols in FIG. 4 are for the steel material (No. 11) with the as-quenched structure. From FIGS. 3 and 4, it can be seen that excellent wear resistance can be obtained if the volume fraction X of iron carbide and the Vickers hardness Hv of the steel material satisfy the relational expression (1).

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Abstract

L'invention concerne un matériau d'acier pour composants coulissants qui présente d'excellentes propriétés de glissement et une excellente aptitude au façonnage. Le matériau d'acier pour composants coulissants : comprend un matériau d'acier ayant une teneur de 0,30 % à 0,60 % en masse de C ; a une structure qui comprend du carbure de fer et au moins soit de la baïnite soit de la martensite revenue ; a un total, en fraction volumique, d'au moins 80 % de baïnite et de martensite revenue et d'au moins 2,0 % de carbure de fer ; et a une dureté Vickers Hv de 300 à 600. La fraction volumique X du carbure de fer et la dureté Vickers Hv satisfont l'expression relationnelle (1).　X ≥ –0,065 × Hv + 36,5 (1). L'unité pour X est le % et l'unité pour Hv est le Hv.
PCT/JP2022/039894 2021-11-08 2022-10-26 Matériau d'acier pour composants coulissants et procédé de production de matériau d'acier pour composants coulissants WO2023080029A1 (fr)

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Citations (5)

* Cited by examiner, † Cited by third party
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JP2006009145A (ja) * 2004-05-24 2006-01-12 Komatsu Ltd 転動部材およびその製造方法
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JP2007308772A (ja) * 2006-05-19 2007-11-29 Kobe Steel Ltd 浸炭部品およびその製造方法
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