US20160138151A1 - Steel Part and Method for Manufacturing the Same - Google Patents

Steel Part and Method for Manufacturing the Same Download PDF

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Publication number
US20160138151A1
US20160138151A1 US14/897,113 US201314897113A US2016138151A1 US 20160138151 A1 US20160138151 A1 US 20160138151A1 US 201314897113 A US201314897113 A US 201314897113A US 2016138151 A1 US2016138151 A1 US 2016138151A1
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Prior art keywords
layer
layers
steel
member under
carbon
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Abandoned
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US14/897,113
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English (en)
Inventor
Kousuke Kuwabara
Minseok Park
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Hitachi Ltd
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Hitachi Ltd
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Publication of US20160138151A1 publication Critical patent/US20160138151A1/en
Abandoned legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/60—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using solids, e.g. powders, pastes
    • C23C8/62—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using solids, e.g. powders, pastes only one element being applied
    • C23C8/64—Carburising
    • C23C8/66—Carburising of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
    • C23C4/06—Metallic material
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C24/00—Coating starting from inorganic powder
    • C23C24/02—Coating starting from inorganic powder by application of pressure only
    • C23C24/04—Impact or kinetic deposition of particles
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/048—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material with layers graded in composition or physical properties
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
    • C23C4/18—After-treatment

Definitions

  • the present invention relates to a steel part and a method for manufacturing the same.
  • machine parts such as drive parts, gears, and bearings are always exposed. to heavy loads, they need to have high mechanical strength such as hardness and fatigue resistance.
  • These machine parts are made from steels used for machine structures such as carbon steel, chromium. steel, chromium molybdenum steel, and nickel chromium-molybdenum steel.
  • the steels used for machine structures may need two opposite properties for an outer portion and an inner par Lion, that is, a surface of the steels needs high fatigue resistance and the material itself needs high fracture resistance to secure shock resistance of the part.
  • the material may have a base material having a comparatively low carbon concentration and a high fracture resistance, for example, a low alloy steel (such as SCM415 defined in JIS-G4104).
  • the surface of the material is often solid-soluted with carbon so as to increase the carbon concentration, and carburizing treatment and carbonitriding treatment are often performed to improve hardness and fatigue resistance.
  • PTL 1 discloses a method for forming a hard film of high carbon steel or a high-carbon low-alloy steel on a surface of a base material and thermally diffuse-bonding the base material and the hard film so as to secure desired strength.
  • An object of the present invention is to prevent the member under treatment and the surface hard layer from peeling off.
  • the member under treatment and the surface hard layer can be prevented from peeling off.
  • FIG. 1 is an example of a block diagram of a steel part.
  • FIG. 2 is an example of a block diagram of the steel part.
  • FIG. 3 is an example of a process drawing showing a process for forming a first layer and a second layer on a member under treatment.
  • FIG. 4 is an example of a schematic diagram showing a steel part according to a second example.
  • FIG. 5 is an example of a schematic diagram showing a cross section of the steel part according to the second example.
  • FIG. 6 is an example of a process drawing showing a process for forming a steel part according to the second example.
  • a steel part according to the present invention includes a plurality of layers having high carbon concentrations than that of a member under treatment (high carbon steel layers) formed on the surface of the member under treatment (steel, part).
  • the carbon concentrations of the high carbon steel layers are 1.0 wt. % or less.
  • the outermost layer has the highest carbon concentration.
  • FIG. 1 shows an embodiment of the present invention.
  • a first layer 102 and a second layer 103 are successively laminated on at least part of a member under treatment 101 so as to form a steel part 100 .
  • the first layer 102 and the second layer 103 are high carbon steel layers having carbon concentrations of 1.0 wt. % or less.
  • the carbon concentrations of the first layer 102 and the second layer 103 are higher than that of the member under treatment.
  • the carbon concentration of the second layer is higher than that of the first layer.
  • FIG. 2 shows another embodiment.
  • a third layer 104 is laminated on the second layer of the steel part shown in FIG. 1 .
  • the carbon concentration of the third layer 104 is higher than that of the second laver.
  • the carbon concentration of the third layer 104 is 1.0 wt. % or less.
  • Examples of the member under treatment on which a surface treatment is performed includes low carbon steel or low carbon alloy steel.
  • the materials having high fracture resistance such as chromium steel, chromium molybdenum steel, chromium molybdenum nickel steel, chromium manganese steel, and chromium nickel, steel (stainless steel) are exemplified, and alloy compositions thereof are defined in domestic and foreign standards such as JIS and ASTM.
  • the plurality of high carbon steel layers coating the member under treatment is required to have carbon concentrations that are higher than that of the member under treatment and 1.0 wt. % or less. Since the carbon concentrations of these layers are higher than that of the member under treatment, these layers have higher fatigue resistances. In addition, when the carbon concentrations of these layers are 1.0 wt. % or less, mesh-shaped cementite can be prevented from excessively deposited on a grain boundary. Thus, the surface can be prevented from embrittling, and as a result, these high carbon steel layers become long fatigue-life layers.
  • the high carbon steel lavers have at least the first layer and the second layer. When necessary, the high carbon steel layers also have one or more layers formed on the first and second layers. The carbon concentration increases from the member under treatment toward the outermost layer.
  • a plurality of layers is formed to decrease differences of carbon concentrations between the layers, and therefore, peeling between the member under treatment and the high carbon steel layer and peeling, cracking and the like between the high carbon steel, layers can be reduced.
  • the desired carbon concentrations and thicknesses of the layers can be freely adjusted.
  • Alloy compositions other than carbon of individual layers are not restricted.
  • these steel materials are high carbon steel and high carbon alloy steel.
  • the compositions of alloy elements of the first layer, the second layer, and at least one layer formed thereon if necessary are nearly the same as that of the member under treatment, so that the high carbon steel layers can be unified with the member under treatment and that a conjugated compound can be prevented from locally being formed.
  • other alloy elements may be adjusted so as to improve properties such as corrosive resistance and heat resistance other than fatigue resistance, at the same time.
  • the plurality of high carbon steel layers may be formed on the entire surface of the member under treatment with equal thicknesses
  • the plurality of high carbon steel layers may have a thickness distribution on the surface of the member under treatment, and may be formed only on part of the member under treatment.
  • each of the layers may be formed only at a portion that needs especially high fatigue resistance such as a contact portion with a bearing of a shaft, tooth of a gear, a contact portion with a member of a press roll.
  • each of the layers may be formed on the surface of the member under treatment with distribution such as a portion having no layers, a portion having only the first layer, and a portion having both the first layer and the second layer.
  • at least one layer formed on the second layer may be formed on part of the surface of the member under treatment.
  • the plurality of high carbon steel layers can be formed according to various methods. As methods that are excellent in forming speed and adherence to the member under treatment, a cold spraying method, a warm spraying method, a plasma spraying method, an arc spraying method, a flame spraying method, a building-up welding method, an aerosol deposition method, and so forth are known.
  • FIG. 3 shows a process for successively forming individual layers.
  • a member under treatment 101 is prepared to form high carbon steel layers.
  • a first layer 102 is formed on the member under treatment 101 .
  • Materials of the individual layers are prepared in the form of powder, wires, rods, and the like, according to the individual methods. According to the method shown in FIG. 3 , powder is sprayed to be deposited on the member under treatment.
  • the layer is formed according to the foregoing method.
  • the carbon concentration of the first powder is higher than that of the member under treatment and 1.0 wt. % or less.
  • the first powder may be a mixture of carbon and another powder.
  • the carbon concentration of the layer contained in the entire layer may be higher than that of the member under treatment and 1.0 wt. % or less.
  • a second layer 102 is formed on the first layer 102 .
  • the second layer is formed on the first layer 102 using powder (second powder) having a higher carbon concentration than that of the first layer.
  • the second. powder may be a mixture of carbon and another powder.
  • the carbon concentration of the entire layer may be higher than that of the first layer and 1.0 wt. % or less.
  • the mixing ratios of a plurality of types of powders having different carbon concentrations are changed, because the kinds of materials required for forming the layer.
  • film forming conditions are appropriately adjusted depending on a method, a member under treatment, and materials of individual layers that are used, it is preferable to form the layer at a temperature of the member under treatment higher than the room temperature, because the film forming efficiency is improved, adherence of each of the layers to the member under treatment is improved, and mutual diffusion on the interface of each of the layers is accelerated.
  • the film forming temperature is adjusted depending on various conditions such as heat resistances and oxidizing resistances of the materials of the member under treatment and the individual layers.
  • FIG. 1 is a block diagram of the steel part 100 in the present example.
  • the member under treatment 101 used for the steel part 100 was a stainless steel plate having a length of 50 mm, a width of 50 mm, and a. thickness of 10 mm (JIS standard: SUS 304, NISSHIN STEEL CO., LTD, 0.05 wt. %).
  • the first layer 102 and the second layer 103 were made from stainless steel powder (DAP304L, DAIDO STEEL LTD). Two types of powder, stainless steel powder A that is additive free and stainless steel powder B that holds graphite powder of 2.0 wt. % (SIGMA-ALDRICH CO. LLC) were mixed at predetermined weight ratios to prepare material powders of the first layer 102 and the second layer 103 .
  • FIG. 1 is a schematic diagram showing individual layers so that they can be easily distinguished. Table 1 lists real thicknesses of individual films that are formed. Theoretically, the carbon concentrations when the powder is adjusted matches the carbon concentrations of the formed layers. However, since carbon is lost while materials are adjusted and layers are formed, the carbon concentrations of the layers are slightly lower than those of the material powders.
  • FIG. 3 shows a process for forming the first layer and the second layer in the present example.
  • the first layer and the second layer were formed by a cold spraying method under the condition that nitrogen gas was used as carrier gas at a pressure of 4 MPa, the temperature of the member under treatment was 400° C., and the nozzle distance was 20 mm.
  • nitrogen gas was used as carrier gas at a pressure of 4 MPa
  • the temperature of the member under treatment was 400° C.
  • the nozzle distance was 20 mm.
  • material powders were changed and the second layer was formed by the cold spraying method in the same conditions.
  • the heat treatment was performed at 800° C. for 30 minutes so that graphite powder held on stainless steel powder B was solidified in each of the layers and then quenching is performed at a speed of 100° C. per second to form the steel part 100 .
  • Example 1 In the configuration of Example 1, a first layer having a carbon concentration of 0.8 wt. % was formed by the cold spraying method, and a second layer was not formed.
  • the other forming conditions were the same as those of Example 1.
  • Example 1 also in a Falex test conducted with a test piece of around 1 mm thick and Vickers hardness (Hv) of 920 on the surface of the steel part 100 , the surface treatment layer having good adherence without inter-laver peeling can be obtained.
  • Hv Vickers hardness
  • FIG. 4 is a schematic diagram of the steel part 100 .
  • the steel cart 100 used a member under treatment 101 of chrome molybdenum steel (JIS standard.: SCM 415, DAIDO STEEL CO., LTD., 0.15 wt. %) having a diameter of 30 mm and a length of 300 mm.
  • a first layer 102 , a second layer 103 , and a third layer 104 were formed at an end portion of the member under treatment.
  • FIG. 5 is a sectional view taken along a line A-A′ of FIG. 4 .
  • FIG. 5 shows a cross section to a line C-C.
  • the first layer 102 , the second layer 103 , and the third layer 104 were formed at the end portion of the member under treatment 101 . All the three layers were formed within 100 mm from the end portion, the first layer 101 and the second layer 102 were formed at the portion between 100 mm and 110 mm from the end portion, and only the first layer 101 was formed at the portion between 110 mm and 120 mm from the end portion of the member under treatment 101 .
  • FIG. 4 is a schematic diagram showing individual layers so that they can be easily distinguished. Table 2 lists real thicknesses of individual films that are formed.
  • chrome molybdenum steel powder A is made of chrome molybdenum steel powder (SCM 415, EPSON ATMIX CORPORATION) that has the same composition as that of the member under treatment 101
  • chrome molybdenum steel powder B is made by increasing only the carbon concentration of the chrome molybdenum steel powder A to 2.0 wt. %, to prepare the material powders of these layers.
  • FIG. 6 shows a process for forming the first layer, the second layer, and the third layer in the present example.
  • Each of the layers were formed using a plasma spraying method.
  • the first layer, the second layer, and the third layer formed in this order by changing the material powders in the same conditions.
  • the member under treatment 101 was scanned by a thermal spray nozzle 106 to form the individual layers at desired portions as shown in FIG. 6 .
  • the other forming conditions were same as those of Example 2.
  • the other forming conditions of Comparative Example 2 were the same as those of Example 2.
  • the other forming conditions of Comparative Example 3 were the same as those of Example 2.
  • the steel parts 100 obtained in Examples 2 and 3 and Comparative Examples 2 and 3 were smoothened by a mechanical polishing method or a buffing method so that the surface roughness (Ra) became 1.0 ⁇ m or less. Thereafter, a Falex test was conducted in lubrication oil for a film-forming portion of the third layer 103 based on ASTM-D-3233.
  • Table 2 shows the thicknesses of the individual layers measured by cutting the steel parts 100 after the Falex test was confucted, average carbon concentrations measured by an electron beam micro-analyzer (SHIMAZU CORPORATION), presence or absence of inter-layer peeling observed by an optical microscope, surface roughness (Ra) of the outermost layers, and cross-sectional Vickers hardness measured by a micro Vickers hardness meter (SHIMAZU CORPORATION).
  • Comparative Example 2 In contrast, in Comparative Example 2, there was a problem in adherence due to small peeling between the member under treatment 101 and the first layer 102 . Further, it was confirmed that in the conditions of Comparative Example 3, the surface roughness after the Falex test was conducted was larger than that of the other steel parts, and the steel part 100 was damaged by abrasion. As a result of an observation of the composition, it was confirmed that mesh-shaped cementite that was characteristic of hypereutectoid steel of a steel material was deposited on a grain boundary, and an carburized portion was damaged.
  • the steel parts having configurations disclosed in the present invention have a surface treatment layer having excellent surface hardness and excellent adherence to a member under treatment.
  • a shaft as a machine part has been described in this section, it is clear that the embodiments of the present invention can be applied to various machine parts such as drive parts, gears, and bearings.
  • VICKERS HARDNESS 940 930 960 (Hv) SURFACE ROUGHNESS (Ra, ⁇ m) 1.1 0.9 2.1 5.4 ADHERENCE BETWEEN BASE NO NO CRACKING NO MATERIAL AND LAYER PEELING PEELING PEELING

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Inorganic Chemistry (AREA)
  • Other Surface Treatments For Metallic Materials (AREA)
  • Coating By Spraying Or Casting (AREA)
US14/897,113 2013-06-10 2013-06-10 Steel Part and Method for Manufacturing the Same Abandoned US20160138151A1 (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2013/065916 WO2014199423A1 (ja) 2013-06-10 2013-06-10 鉄鋼部材および鉄鋼部材の製造方法

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US (1) US20160138151A1 (ja)
JP (1) JP6062048B2 (ja)
CN (1) CN105308213A (ja)
AU (1) AU2013392321B2 (ja)
WO (1) WO2014199423A1 (ja)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102018203637A1 (de) 2018-03-09 2019-09-12 Volkswagen Aktiengesellschaft Gestaltung des Übergangs von Laserauftragsschweißgut zu Substrat zur Verminderung der Kerbwirkung
EP3933067A1 (de) * 2020-07-03 2022-01-05 Flender GmbH Verfahren zur herstellung einer beschichtung, eine beschichtung, ein bauteil mit einer beschichtung

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20220403539A1 (en) * 2019-12-20 2022-12-22 Nippon Steel Corporation Ni-PLATED STEEL SHEET, AND METHOD FOR MANUFACTURING Ni-PLATED STEEL SHEET
CN113957434B (zh) * 2021-10-22 2022-11-04 燕山大学 一种在低碳钢表面制备高硬度高耐磨熔覆层的方法

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DE3315556C1 (de) * 1983-04-29 1984-11-29 Goetze Ag, 5093 Burscheid Verschleissfeste Beschichtung
US6048586A (en) * 1996-06-05 2000-04-11 Caterpillar Inc. Process for applying a functional gradient material coating to a component for improved performance
DE102006023690A1 (de) * 2006-05-19 2007-11-22 Schaeffler Kg Verfahren zur Herstellung eines Wälzlagerbauteils sowie Wälzlagerbauteil
JP5605901B2 (ja) * 2010-09-30 2014-10-15 国立大学法人東北大学 コールドスプレー法による金属材料の補修方法及びコールドスプレー用粉末材料の製造方法、並びに、コールドスプレー皮膜

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102018203637A1 (de) 2018-03-09 2019-09-12 Volkswagen Aktiengesellschaft Gestaltung des Übergangs von Laserauftragsschweißgut zu Substrat zur Verminderung der Kerbwirkung
EP3933067A1 (de) * 2020-07-03 2022-01-05 Flender GmbH Verfahren zur herstellung einer beschichtung, eine beschichtung, ein bauteil mit einer beschichtung

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WO2014199423A1 (ja) 2014-12-18
JP6062048B2 (ja) 2017-01-18
AU2013392321B2 (en) 2016-09-29
JPWO2014199423A1 (ja) 2017-02-23
AU2013392321A1 (en) 2016-01-07
CN105308213A (zh) 2016-02-03

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