WO2018093146A1 - Procédé de revêtement d'un alliage à base de fer et produit ainsi obtenu ayant une dureté élevée et une propriété à coefficient de frottement réduit - Google Patents

Procédé de revêtement d'un alliage à base de fer et produit ainsi obtenu ayant une dureté élevée et une propriété à coefficient de frottement réduit Download PDF

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Publication number
WO2018093146A1
WO2018093146A1 PCT/KR2017/012944 KR2017012944W WO2018093146A1 WO 2018093146 A1 WO2018093146 A1 WO 2018093146A1 KR 2017012944 W KR2017012944 W KR 2017012944W WO 2018093146 A1 WO2018093146 A1 WO 2018093146A1
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chromium
iron
based alloy
coating layer
layer
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PCT/KR2017/012944
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English (en)
Korean (ko)
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김상권
이재훈
여국현
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한국생산기술연구원
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Priority to CN201780071249.3A priority Critical patent/CN109983147B/zh
Publication of WO2018093146A1 publication Critical patent/WO2018093146A1/fr

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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
    • C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
    • C23C10/28—Solid state diffusion of only metal elements or silicon into metallic material surfaces using solids, e.g. powders, pastes
    • C23C10/34—Embedding in a powder mixture, i.e. pack cementation
    • C23C10/36—Embedding in a powder mixture, i.e. pack cementation only one element being diffused
    • C23C10/38—Chromising
    • C23C10/40—Chromising 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
    • C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
    • C23C10/60—After-treatment
    • 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
    • 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
    • C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
    • C23C28/34—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/36—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases using ionised gases, e.g. ionitriding

Definitions

  • the present invention relates to a method for coating an iron-based alloy and a product having high hardness and low friction characteristics, and more particularly, after forming a chromium-based coating layer by pack cementation on the surface of the iron-based alloy, the chromium-based coating layer is
  • the present invention relates to a coating method of an iron-based alloy for coating an iron-based alloy layer by screen plasma immersion carbonization on a formed iron-based alloy, and a product having high hardness and low friction characteristics.
  • pack cementation is a kind of chemical vapor deposition (CVD) technique, in which an iron-based alloy and a pack mixture powder are charged into a pack, and then the pack is heated to coat the iron-based alloy.
  • the pack mixture powder is a powder containing a reactive metal such as chromium (Cr), aluminum (Al), silicon (Si), etc., an active agent such as ammonium chloride (NH 4 Cl), and an inert such as alumina (Al 2 O 3 ). to be.
  • a reactive metal such as chromium (Cr), aluminum (Al), silicon (Si), etc.
  • an active agent such as ammonium chloride (NH 4 Cl)
  • an inert such as alumina (Al 2 O 3 ).
  • Pack cementation is a coating method that has been used for a long time and has many advantages.
  • Pack cementation is a coating method for forming a coating layer that is simple, economical and has good adhesion.
  • the iron-based alloy coated by the pack cementation has mechanical properties such as improved hardness, corrosion resistance, wear resistance, oxidation resistance and the like.
  • a uniform coating layer may be formed on the entire surface of the iron-based alloy having a three-dimensional shape by pack cementation.
  • Pack cementation may be classified into chromizing, aluminizing, siliconizing, etc. according to the kind of reactive metal.
  • Patent No. 10-1384374 name of the invention: a method for coating a metal sintered part by pack cementation and a pack cementation coated metal sintered part, Patent Document 1 is disclosed.
  • US Patent Publication No. 2011-0293365 name: Cement plant refractory anchor, Patent Document 2
  • US Patent No. 5275983 Pack name of the invention: Pack mixture composition for SiC pack cementation coating of carbonaceous substrates, Patent Document 3 is disclosed.
  • parts such as bearings and bushings are used in a device that rotates at high speed, and require low friction characteristics as well as high hardness surfaces.
  • iron-based alloys have a high hardness surface but have a high friction coefficient to be used as materials for bearings and bushings.
  • a screen plasma method is used to penetrate nitrogen atoms and carbon atoms to improve hardness and reduce friction coefficients by forming new carbide and nitride complexes on the surface of iron-based alloys.
  • Screen plasma immersion carbonization is a method of generating plasma directly on the surface of an iron-based alloy to penetrate nitrogen and carbon. Unlike the conventional plasma method, plasma is generated through a screen separated from the iron-based alloy to infiltrate nitrogen to form an immersion carbonization layer. It is a method of manufacturing.
  • the screen plasma apparatus includes a vacuum chamber 10, a screen 20, a heater 30, a vacuum pump 40, a cathode power supply 50, and a heater power supply 60.
  • a general screen plasma precipitated carbonization is described.
  • the vacuum chamber 40 is operated to create a vacuum pressure atmosphere of about 1 ⁇ 10 -3 Torr in the vacuum chamber 10, and then the cathode power supply unit 50 connected to the screen 20 is operated to operate the screen.
  • the heater 20 is heated and the heater 30 is connected to the heater 30 so that the heater 30 is heated to raise the temperature in the vacuum chamber 10 to the process temperature.
  • the inner wall of the vacuum chamber 10 shows a positive (+) relative charge
  • the screen 20 shows a negative (-) relative charge, so that an electric field is generated between the inner wall of the vacuum chamber 10 and the screen 20.
  • nitrogen, hydrocarbon and hydrogen gas are injected into the vacuum chamber 10.
  • the hydrogen gas is formed in a high temperature and a vacuum atmosphere inside the vacuum chamber 10, and as soon as it is injected into the vacuum chamber 10 receives the energy of the temperature and pressure is plasmaized, hydrogen plasma and hydrocarbon plasma is screened (20) Dense around.
  • Nitrogen gas has a relatively high ionization energy than hydrogen gas, and thus, plasma is not smoothed. However, the plasma plasma hydrogenated already collides with the nitrogen gas and serves to smoothly generate the nitrogen plasma.
  • Screen plasma immersion carbonization using the screen plasma apparatus as described above has a problem of heating the vacuum chamber by using a heater, which is an additional device, to increase the temperature of the vacuum chamber to the process temperature.
  • a heater which is an additional device
  • the iron-based oxide film is naturally formed on the surface, which causes the iron-based oxide film to inhibit the nitriding carbonization process, and there is a problem that the iron-based oxide film is removed by lowering the magnetic conductivity of the iron-based alloy.
  • the conventional screen plasma apparatus applies a high-current power source and applies a cathodic, so that a high-density input process of the penetrating element is not possible due to the reaction of nitrogen and hydrocarbon gas in the glow, thereby accelerating the particle accelerator.
  • a high voltage is applied to the device to form an immersion layer on the iron-based alloy.
  • Patent Document 1 Republic of Korea Patent No. 10-1384374
  • Patent Document 2 United States Patent Publication No. 2011-0293365
  • Patent Document 3 US Patent No. 5275983
  • the technical problem to be achieved by the present invention is to control a strong oxide film, such as Cr 2 O 3 is naturally formed in a stainless steel material that can be removed only by processing outside the conventional pickling operation, while a very small amount without a separate external heater in the heating process It is to provide an iron-based alloy coating method using a heating process using a glow (glow) formed on the screen by the amount of gas input and power. Specifically, it aims to provide a new alloy coating on the outermost surface of the coating layer using nitrogen and carbon in atomic units, and to provide a product having high hardness and low friction characteristics manufactured by the above method.
  • an embodiment of the present invention is to form a chromium-based coating layer on the surface of the iron-based alloy using the pack cementation, and to form an impregnated carbonization layer using a screen plasma on the chromium-based coating layer It provides an iron-based alloy coating method comprising the step of.
  • the iron-based alloy may be an iron-based alloy coating method characterized in that it comprises a bearing steel or stainless steel.
  • the chromium-based coating layer is characterized in that it contains chromium (Cr), chromium (Cr) and iron (Fe) or chromium (Cr), iron (Fe) and vanadium (V) Alloy coating method.
  • the step of forming a chromium-based coating layer on the surface of the iron-based alloy using the pack cementation the step of injecting the iron-based alloy and the pack mixture in a pack (pack), charging the pack into a vacuum chamber
  • a chromium-based coating layer forming step of forming a chromium-based coating layer on the iron-based alloy while heating is maintained in the charging step a heating step of heating the pack charged in the vacuum chamber, and the heating step, wherein the pack mixture is formed of chromium.
  • It may be an iron-based alloy coating method comprising a powder, an active agent and an inert agent.
  • the chromium-based powder of the pack mixture is chromium (Cr) powder, chromium (Cr) powder and iron (Fe) powder or chromium (Cr) powder, iron (Fe) powder and vanadium (V) It may be an iron-based alloy coating method characterized in that it comprises a powder.
  • the pack mixture is characterized in that it comprises 10.5 wt% to 52.9 wt% of the chromium-based powder, 0.1 wt% to 3 wt% of the active agent and 47 wt% to 89.4 wt% of the inert agent. It may be an iron-based alloy coating method.
  • the step of forming the nitriding carbide layer using the screen plasma on the chromium-based coating layer, charging the iron-based alloy coated with the chromium-based coating layer in a vacuum chamber and covers the iron-based alloy with a double screen The ion cleaning step of reducing the chromium-based oxide film present on the iron-based alloy by injecting a first hydrogen gas into the vacuum chamber, a process current is applied to the dual screen and the second hydrogen gas, nitrogen in the vacuum chamber Generating a mixed plasma by injecting a gas and a hydrocarbon gas; and coating the mixed plasma on a chromium-based coating layer formed on the surface of the iron-based alloy to form an impregnated carbonized layer.
  • the ion cleaning step includes applying a first current to the dual screen to heat the vacuum chamber, injecting first hydrogen into the vacuum chamber, and applying the second screen to the dual screen. Generating a hydrogen plasma around the dual screen by applying a current; and reducing and removing the chromium-based oxide film present on the iron-based alloy.
  • the first current may be 3 A to 5 A and the second current may be iron-based alloy coating method, characterized in that 5 A to 15 A.
  • the chromium-based oxide film is characterized in that it contains chromium (Cr), chromium (Cr) and iron (Fe) or chromium (Cr), iron (Fe) and vanadium (V) Alloy coating method.
  • the process current may be an iron-based alloy coating method, characterized in that 20 to 30 A.
  • the content ratio of the nitrogen gas to hydrogen gas may be an iron-based alloy coating method, characterized in that 1: 3 to 4: 1.
  • the hydrocarbon gas may be an iron-based alloy coating method, characterized in that the CH 4 or C 2 H 2 and 1 sccm to 10 sccm gas amount is pulse-injected by repeating the injection section and the stop section. have.
  • another embodiment of the present invention provides a product having a high hardness and low friction characteristics produced by the iron-based alloy coating method.
  • the hardness of the product may be a product having high hardness and low friction characteristics, characterized in that 1450 HV to 2400 HV.
  • the friction coefficient of the product may be a product having a high hardness and low friction characteristics, characterized in that 0.3 to 0.4.
  • glow discharge can be formed around the screen at a high density, so that the inside of the vacuum chamber can be sufficiently raised to the process temperature without a heater.
  • the precipitated carbonization process may not be inhibited by removing the chromium-based oxide film present on the iron-based alloy using the ion cleaning process in the screen plasma process.
  • the product manufactured by the iron-based alloy coating method has a hardness value of 1450 HV or more hardness, it may have a characteristic that the friction coefficient can be lowered to 0.4 or less.
  • FIG. 1 is a cross-sectional view showing a conventional screen plasma apparatus.
  • FIG. 2 is a cross-sectional view showing a screen plasma apparatus according to an embodiment of the present invention.
  • FIG 3 is a perspective view of a dual screen according to an embodiment of the present invention.
  • FIG. 4 is a graph showing X-ray diffraction patterns of SUJ2 having a chromium-based coating layer and a precipitated carbonization layer according to an embodiment of the present invention.
  • FIG. 5 is a graph showing X-ray diffraction patterns of SUJ2 having a chromium-based coating layer and a carburized layer according to an embodiment of the present invention.
  • FIG. 6 is a graph showing X-ray diffraction patterns of SUS316 having a chromium-based coating layer and a precipitated carbonization layer according to an embodiment of the present invention.
  • FIG. 7 is a graph illustrating X-ray diffraction patterns of SUS316 having a chromium-based coating layer and a carburized layer according to an embodiment of the present invention.
  • FIG. 9 is a graph showing the element content according to the depth of Preparation Example 1 (SUJ2-Cr-SPNC) according to an embodiment of the present invention.
  • FIG. 10 is an image showing a cross-sectional shape of Preparation Example 2 (SUJ2-Cr-Fe-SPNC) according to an embodiment of the present invention.
  • FIG. 11 is a graph showing the element content according to the depth of Preparation Example 2 (SUJ2-Cr-Fe-SPNC) according to an embodiment of the present invention.
  • FIG. 12 is an image showing a cross-sectional shape of Preparation Example 3 (SUJ2-Cr-Fe-V-SPNC) according to an embodiment of the present invention.
  • FIG. 13 is a graph showing the element content according to the depth of Preparation Example 3 (SUJ2-Cr-Fe-V-SPNC) according to an embodiment of the present invention.
  • Comparative Example 1 (SUJ2-Cr-SPC) according to an embodiment of the present invention.
  • Comparative Example 1 (SUJ2-Cr-SPC) according to an embodiment of the present invention.
  • Comparative Example 4 (SUJ2-Cr-Fe-SPC) according to an embodiment of the present invention.
  • FIG 17 is a graph showing the element content according to the depth of Comparative Example 4 (SUJ2-Cr-Fe-SPC) according to an embodiment of the present invention.
  • Comparative Example 5 (SUJ2-Cr-Fe-V-SPC) according to an embodiment of the present invention.
  • FIG. 20 is an image showing a cross-sectional shape of Preparation Example 4 (SUS316-Cr-SPNC) according to an embodiment of the present invention.
  • FIG. 21 is a graph showing the element content according to the depth of Preparation Example 4 (SUS316-Cr-SPNC) according to an embodiment of the present invention.
  • FIG. 22 is an image showing a cross-sectional shape of Preparation Example 5 (SUS316-Cr-Fe-SPNC) according to an embodiment of the present invention.
  • FIG. 23 is a graph showing the element content according to the depth of Preparation Example 5 (SUS316-Cr-Fe-SPNC) according to an embodiment of the present invention.
  • 25 is a graph showing the element content according to the depth of Preparation Example 6 (SUS316-Cr-Fe-V-SPNC) according to an embodiment of the present invention.
  • Figure 26 is an image showing the cross-sectional shape of Comparative Example 6 (SUS316-Cr-SPC) according to an embodiment of the present invention.
  • FIG. 27 is a graph showing the element content according to the depth of Comparative Example 6 (SUS316-Cr-SPC) according to an embodiment of the present invention.
  • Comparative Example 8 SUS316-Cr-Fe-V-SPC
  • FIG. 31 is a graph showing the element content according to the depth of Comparative Example 8 (SUS316-Cr-Fe-V-SPC) according to an embodiment of the present invention.
  • 35 is a graph illustrating a friction coefficient of Comparative Example 1 (SUJ2-Cr-SPC) according to an embodiment of the present invention.
  • FIG. 36 is a graph illustrating a friction coefficient of Comparative Example 4 (SUJ2-Cr-Fe-SPC) according to an embodiment of the present invention.
  • 40 is a graph measuring the coefficient of friction of Preparation Example 4 (SUS316-Cr-SPNC) according to an embodiment of the present invention.
  • FIG 43 is a graph illustrating a coefficient of friction of Comparative Example 6 (SUS316-Cr-SPC) according to an embodiment of the present invention.
  • Example 44 is a graph illustrating a friction coefficient of Comparative Example 7 (SUS316-Cr-Fe-SPC) according to an embodiment of the present invention.
  • first component is expressed as being “connected (connected, contacted, coupled)" to a second component, it is said that the first component is “directly connected” to the second component or a third component. Means that it can be “indirectly connected” through. Singular expressions include plural expressions unless the context clearly indicates otherwise. Also, the terms “comprise” or “have” mean that there is a feature, number, step, operation, component, part, or combination thereof described in the specification, but one or more other features, It does not mean that the presence or addition of numbers, steps, operations, components, parts, or combinations thereof is excluded.
  • the iron-based alloy coating method is to form a chromium-based coating layer on the surface of the iron-based alloy using the pack cementation, and forming a nitriding carbonized layer using a screen plasma on the chromium-based coating layer It may include.
  • a chromium-based coating layer is formed on the iron-based alloy surface by using pack cementation.
  • the method for forming a chromium-based coating layer on the surface of the iron-based alloy using the pack cementation may include a charging step, a heating step of heating the pack charged in the vacuum chamber, and a chromium-based coating layer forming step of forming a chromium-based coating layer on the iron alloy while the heating is maintained in the heating step.
  • the iron-based alloy and the pack mixture are first introduced into a pack.
  • Pack cementation is a method of manufacturing a coating layer in which a metal part to be processed is put into a pack mixture and heated at a high temperature for a predetermined time to form a surface layer on the metal part, and at the same time obtain a diffusion coating layer on the surface layer of the metal part.
  • Pack cementation of the present invention can be used as a method for forming a chromium-based coating layer on the surface of the iron-based alloy.
  • the iron-based alloy may include, but is not limited to, bearing steel or stainless steel.
  • the bearing steel is a high carbon chromium special steel
  • the stainless steel is an alloy steel containing nickel and chromium to supplement the corrosion resistance of iron.
  • the iron-based alloy of the present invention may be SUJ2 bearing steel or SUS316 stainless steel.
  • the pack mixture may include a chromium-based powder, an active agent and an inert agent.
  • the chromium-based powder of the pack mixture is chromium (Cr) powder, chromium (Cr) powder and iron (Fe) powder or chromium (Cr) powder, iron (Fe) powder and vanadium (V) It may include a powder, but is not limited thereto.
  • the chromium-based powder of the present invention is a reactant used when preparing a chromium-based coating layer, and may improve hardness, corrosion resistance, and lubricity of an iron-based alloy. It can be effective.
  • the active agent in the present invention may contribute to the formation of the chromium-based coating layer while reacting with the chromium powder to form a chromium-based coating layer, it may include a halogenated compound salt.
  • the halogenated compound salt may include potassium tetrafluoroborate (KBF 4 ), ammonium chloride (NH 4 Cl), fluoroammonium (NH 4 F), fluorine sodium (NaF) or sodium chloride (NaCl), It is not limited to this.
  • the active agent of the present invention may be potassium tetrafluoroborate (KBF 4 ).
  • the inert agent of the present invention can prevent the sintering of the iron-based alloy in the process of forming the chromium-based coating layer.
  • the inert agent may include, but is not limited to, aluminum oxide (Al 2 O 3 ), silica (SiO 2 ), silicon carbide (SiC) or chromium oxide (Cr 2 O 3 ). .
  • the inert agent of the present invention may be aluminum oxide (Al 2 O 3 ).
  • the pack mixture may include 10.5 wt% to 52.9 wt% of the chromium-based powder, 0.1 wt% to 3 wt% of the active agent, and 47 wt% to 89.4 wt% of the inert agent, but It is not limited.
  • the content of the chromium-based powder may include 10.5 wt% to 52.9 wt% of the total content of the pack mixture.
  • the content of the chromium-based powder is less than 10.5 wt%, the chromium-based coating layer may be formed too thin or the hardness value of the chromium-based coating layer may not reach the target value, which is not preferable.
  • the content of the chromium-based powder is more than 52.9 wt%, the chromium-based powder is agglomerated with the inert agent, and unnecessary substances are added to the surface of the iron-based alloy, which may cause excessive pores in the iron-based alloy, which is not preferable.
  • the content of chromium metal powder of the present invention may be 30 wt%.
  • the content of the active agent may include 0.1 wt% to 3 wt% of the total content of the pack mixture.
  • the content of the activator is less than 0.1 wt% or more than 3 wt%, considering the content of the chromium-based powder described above, a non-uniform chromium-based coating layer is formed or staining occurs inside the chromium-based coating layer, so that the mechanical properties of the chromium-based coating layer The problem of deterioration may arise, which is undesirable.
  • the content of the active agent of the present invention may be 1 wt%.
  • the content of the inert agent may include 47 wt% to 89.4 wt% of the total content of the pack mixture. If the content of the inert agent is less than 47 wt%, the penetration and diffusion of chromium, which will form the chromium-based coating layer, may not be achieved. If the content of the inert agent is more than 89.4 wt%, the formation of the chromium-based coating layer may be delayed. The mechanical properties of the chromium-based coating layer may be less than the target value is not preferable.
  • the content of the inert agent of the present invention may be 69 wt%.
  • the pack loaded in the vacuum chamber is heated.
  • a chromium-based coating layer is formed on the iron-based alloy while the heating process is maintained.
  • the chromium-based coating layer may be formed of a chromium-based halogen compound gas by reacting chromium-based powder of the components constituting the pack mixture with the activator while the heating temperature is maintained, wherein the chromium-based halogen gas is the surface of the iron-based alloy Adsorbed on, it may be formed while penetrating and diffusing into the iron-based alloy.
  • the chromium-based coating layer is formed on the surface of the iron-based alloy by using pack cementation, and then an impregnated carbonization layer is formed on the chromium-based coating layer by using a screen plasma.
  • the screen plasma apparatus includes a vacuum chamber 10, a double screen 70, a vacuum pump 40, and a cathode power supply 50.
  • a vacuum chamber 10 a vacuum chamber 10
  • a double screen 70 a vacuum pump 40
  • a cathode power supply 50 a cathode power supply 50.
  • the method of forming an immersion carbonization layer using the screen plasma on the chromium-based coating layer is charged with the iron-based alloy (2) coated with the chromium-based coating layer in the vacuum chamber 10 and the iron-based alloy Covering (2) with a double screen 70, an ion cleaning step of reducing the chromium-based oxide film present on the iron-based alloy 2 by injecting a first hydrogen gas into the vacuum chamber 10, the double Applying a process current to the screen 70, injecting a second hydrogen gas, nitrogen gas and hydrocarbon gas into the vacuum chamber 10 to generate a mixed plasma and the mixed plasma is formed on the surface of the iron-based alloy (2) It may include the step of coating on the chromium-based coating layer to form a precipitated carbonization layer.
  • the iron-based alloy (2) coated with a chromium-based coating layer is charged into the vacuum chamber 10 and the iron-based alloy (2) is covered with a double screen 70, and then the vacuum pump 40 is operated to operate the vacuum chamber ( 10)
  • the atmosphere inside is formed at a vacuum level of 1 ⁇ 10 -3 Torr to 1 ⁇ 10 -1 Torr.
  • the inner wall of the vacuum chamber 10 shows a positive (+) relative charge
  • the double screen 70 shows a negative (-) relative charge, so that an electric field is formed between the inner wall of the vacuum chamber 10 and the double screen 70. Is generated.
  • the vacuum degree of the vacuum chamber 10 is less than 1 ⁇ 10 ⁇ 1 Torr, it is not preferable that impurities in the vacuum chamber 10 are not sufficiently removed, and impurities are sufficiently formed even if a vacuum atmosphere is formed within 1 ⁇ 10 ⁇ 3 Torr. Since it can be removed, creating a vacuum atmosphere above 1 ⁇ 10 ⁇ 3 Torr is undesirable because it is unnecessary in the process.
  • the iron-based alloy (2) is covered with a double screen (70).
  • FIG 3 is a perspective view of a dual screen 70 according to an embodiment of the present invention.
  • the dual screen 70 is a screen used in a screen plasma process, and includes an outer cylinder 71 and an inner cylinder 72, and has a cylindrical structure with an open bottom.
  • the dual screen 70 may serve as an electrode for generating glow discharge in the vacuum chamber 10.
  • a first hydrogen gas is injected into the vacuum chamber 10 to reduce the chromium-based oxide film present on the iron-based alloy 2, which is called ion cleaning.
  • the internal temperature of the vacuum chamber 10 is raised to 100 ° C.
  • the vacuum chamber 10 when the vacuum chamber 10 is preheated to 100 ° C. by applying a first current, the vacuum chamber 10 is cooled from low to high temperature by using a high density glow generated between the screens. When the temperature change occurs, it is possible to prevent cracking due to thermal expansion, and oxygen and moisture may be discharged while burning the carbon inside the vacuum chamber 10.
  • the first current is 3 A to 5 A.
  • the first current is applied to the dual screen 70 so that the intensity of the first current for heating the internal temperature of the vacuum chamber 10 to 100 ° C is preferably 3 A to 5 A.
  • the first current may be 5 A.
  • the first hydrogen of the present invention may be a gas source for generating a hydrogen plasma.
  • a second current is applied to the dual screen 70 to generate a hydrogen plasma around the dual screen 20.
  • the heating process may be performed to increase the temperature of the vacuum chamber 10 to the process temperature by using a glow formed on the screen with a very small amount of gas input and power without a separate external heater.
  • the hydrogen plasma may comprise hydrogen plasma species including H ⁇ , H ⁇ or H ⁇ .
  • the second current is 5 A to 15 A.
  • the second current may be applied to the dual screen 70 to heat the internal temperature of the vacuum chamber 10 to 250 ° C., and the intensity of the second current that may generate hydrogen plasma is preferably 5 A to 15 A.
  • the first current may be 15 A.
  • the hydrogen plasma may be located in the center of the vacuum chamber by the force of the vacuum pump.
  • the chromium oxide film present on the iron-based alloy 2 is reduced and removed.
  • the iron-based alloy 2 coated with a chromium-based coating layer by pack cementation may have a chromium-based oxide film formed on a surface thereof when contacted with external air before being charged into the vacuum chamber 10.
  • the chromium-based oxide film may be a cause of inhibiting the nitriding carbonization process, the corrosion resistance of the iron-based alloy may be improved, but there is a disadvantage in reducing the magnetic conductivity. Therefore, in the present invention, the hydrogen plasma located at the center of the vacuum chamber 10 may react with the chromium oxide film to reduce and remove the chromium oxide film.
  • the chromium-based oxide film may include chromium (Cr), chromium (Cr) and iron (Fe) or chromium (Cr), iron (Fe) and vanadium (V), but is not limited thereto. It is not intended to be.
  • a process current is applied to the double screen 70, the second hydrogen gas, nitrogen gas and hydrocarbon gas is injected into the vacuum chamber 10 to generate a mixed plasma.
  • the mixed plasma may be nitrogen plasma, hydrogen plasma and hydrocarbon plasma.
  • the process current may be 20 A to 30 A.
  • Process current may be applied to the dual screen 70 to heat the internal temperature of the vacuum chamber 10 to 450 °C to 550 °C to generate the intensity of the process current is preferably 20 A to 30 A. .
  • the second hydrogen gas and the hydrocarbon gas are injected into the vacuum chamber 10
  • the second hydrogen gas and the hydrocarbon gas are formed in the vacuum chamber 10 in a high temperature and a vacuum atmosphere, so that the vacuum chamber 10 As soon as it is injected, it is plasmaized by the energy of temperature and pressure, and the hydrogen plasma and hydrocarbon plasma are concentrated around the double screen 70.
  • the hydrocarbon gas may include CH 4 or C 2 H 2 , and the amount of 1 sccm to 10 sccm gas may be pulse-injected by repeating the injection section and the stop section.
  • the ionization rate of the hydrocarbon gas can be increased by pulse injection of the hydrocarbon gas, and the diffusion layer of carbon and nitrogen can be formed deeper than the same time zone.
  • the hydrogen plasma may include hydrogen plasma species including H ⁇ , H ⁇ , or H ⁇
  • the hydrocarbon gas may be pulse injected by repeating a section in which the gas is injected for 2 seconds and stopped for 5 seconds.
  • the nitrogen gas has a relatively high ionization energy than the hydrogen gas, so that the plasma is not smoothed.
  • the plasma plasma hydrogenated already collides with the nitrogen gas to smoothly generate the nitrogen plasma.
  • the hydrogen plasma may improve the fluidity of the nitrogen plasma.
  • the nitrogen plasma of the present invention may include nitrogen species including N + , N, N 2 + or NH 3 .
  • the content ratio of nitrogen gas to hydrogen gas may be 1: 3 to 4: 1. More preferably, when the iron-based alloy is a bearing steel, the content ratio of nitrogen gas to hydrogen gas is 1: 3 to 1: 2, and in the case of stainless steel, the content ratio of nitrogen gas to hydrogen gas is 1: 1 to 4: 1. desirable.
  • the bearing steel since it is more difficult to diffuse nitrogen into the base material than the stainless steel, it is preferable to induce nitrogen diffusion by increasing the content of hydrogen gas to improve the fluidity of the nitrogen plasma. Therefore, a content ratio of nitrogen gas to hydrogen gas of 1: 3 to 1: 2 in which the content of hydrogen is higher than the content of nitrogen is preferable.
  • the stainless steel it is an iron-based alloy that is advantageous to contain nitrogen, the content of nitrogen gas to hydrogen gas of 1: 1 to 4: 1 where the content of nitrogen is higher than the content of hydrogen in order to perform nitrogen diffusion more densely Rain is preferred.
  • the mixed plasma is coated on the chromium-based coating layer formed on the surface of the iron-based alloy (2) to form an precipitated carbonization layer.
  • the nitrogen plasma and hydrocarbon plasma are located in the center of the vacuum chamber 10 under the influence of the vacuum pump 40, the nitrogen plasma and hydrocarbon plasma is sucked gas by the vacuum pump 40
  • the vacuum pump 40 In order to penetrate the iron-based alloy (2) coated with the chromium-based coating layer located in the center of the vacuum chamber 10 in the direction of the impregnated carbonization layer may be formed on the surface of the iron-based alloy (2).
  • the hardness of the product may be 1450 HV to 2400 HV.
  • the present invention can increase the hardness of the iron-based alloy using a pack cementation and screen plasma process. Therefore, the hardness of the product based on the iron-based alloy prepared in the above process may be 1450 HV to 2400 HV.
  • the friction coefficient of the product may be 0.3 to 0.4.
  • the present invention can reduce the coefficient of friction of the iron-based alloy using a pack cementation and screen plasma process. Therefore, the coefficient of friction of the product based on the iron-based alloy prepared in the above process may be 0.3 to 0.4.
  • a pack mixture including 30 wt% chromium powder, 1 wt% potassium tetrafluoroborate and 69 wt% aluminum oxide was prepared.
  • SUJ2 and the pack mixture were put into a pack, the pack was charged into a vacuum chamber, and the inside of the vacuum chamber was evacuated to a vacuum of 1 Torr.
  • purging was performed by supplying argon gas three times in the vacuum chamber, and lowering the flow rate of the supplied argon gas to maintain the inside of the vacuum chamber at 1 atmosphere.
  • the chromium coating layer was manufactured by maintaining the temperature inside the vacuum chamber at 950 ° C. for 10 hours.
  • the charged SUJ2 After charging the SUJ2 having the chromium coating layer prepared in a vacuum chamber, the charged SUJ2 is covered with a double screen, and the degree of vacuum in the vacuum chamber is maintained at a level of 5 ⁇ 10 ⁇ 3 Torr for 30 minutes. Thereafter, 500 sccm of the first hydrogen gas is added to the vacuum chamber to maintain the vacuum at 0.1 Torr. Next, a current of 5 A is applied to the screen and a high density glow generated between the screens is used to preheat the vacuum chamber to prevent cracking due to thermal expansion when a temperature change occurs from low to high temperatures. Next, a current of 15 A is applied for 30 minutes to raise the temperature inside the vacuum chamber to 250 ° C.
  • chromium, iron and vanadium powder was carried out under the same conditions except that the chromium-iron-vanadium coating layer prepared in the SUS316 to produce a carbonized carbon layer It was.
  • carburizing screen on the coating layer is an iron-based alloy (SUJ2-Cr-SPC) coating prepared
  • a carburized layer was prepared in SUJ2 in which a chromium coating layer was prepared under the same conditions except that nitrogen gas was not used and the hydrocarbon gas was continuously injected in Preparation Example 1.
  • the carburized layer was prepared in SUJ2 under the same conditions except that the pack cementation was not performed in Preparation Example 1, and the nitrogen gas was not used when the screen plasma was used and the hydrocarbon gas was continuously injected.
  • the iron-based alloy (SUJ2-Cr-Fe-SPC) manufactured by coating a carburizing layer on the coating layer
  • the carburized layer was prepared in SUJ2 in which the chromium-iron coating layer was prepared under the same conditions except that nitrogen gas was not used and the hydrocarbon gas was continuously injected in Preparation Example 2.
  • the iron- based alloy (SUJ2-Cr-Fe-V-SPC) having a carburized layer coated on the coating layer was manufactured.
  • Example 3 a carburized layer was prepared in SUJ2 in which a chromium-iron-vanadium coating layer was prepared under the same conditions except for continuously injecting a hydrocarbon gas without using nitrogen gas.
  • an iron-based alloy needle carbide layer is coated (SUS316-Cr-SPC) on the coating layer
  • the carburized layer was prepared in SUS316, in which the chromium coating layer was prepared under the same conditions except that nitrogen gas was not used and the hydrocarbon gas was continuously injected in Preparation Example 4.
  • an iron-based alloy SUS316-Cr-Fe-SPC having a carburized layer coated on the coating layer was manufactured.
  • the carburized layer was prepared in SUS316, in which the chromium-iron coating layer was manufactured under the same conditions except that nitrogen gas was not used and the hydrocarbon gas was continuously injected in Preparation Example 5.
  • Example 6 a carburized layer was prepared on SUS316 in which a chromium-iron-vanadium coating layer was prepared under the same conditions except for continuously injecting a hydrocarbon gas without using nitrogen gas.
  • 4 is a manufacturing example 1 (SUJ2-Cr-SPNC) coated with an immersion carbide layer on SUJ2 coated with a chromium-based coating layer by pack cementation, Preparation Example 2 (SUJ2-Cr-Fe-SPNC) and Preparation Example 3 (SUJ2 X-ray diffraction patterns of -Cr-Fe-V-SPNC).
  • 5 is Comparative Example 1 (SUJ2-Cr-SPC), Comparative Example 4 (SUJ2-Cr-Fe-SPC) and Comparative Example 5 (coated with a carburized layer on SUJ2 coated with a chromium-based coating layer by pack cementation). X-ray diffraction patterns of SUJ2-Cr-Fe-V-SPC).
  • the SUJ2 having the precipitated carbonization layer formed by the screen plasma has a different crystal structure from that of the SUJ2 having the carbonaceous layer formed therein, and the crystal structure differs depending on the chromium-based material for preparing the coating layer by pack cementation. It confirmed that it represents.
  • various desired crystal phases can be produced by using pack cementation and screen plasma.
  • the pack cementation and the screen plasma can be performed together in a process for manufacturing a coating layer on SUJ2.
  • FIG. 6 is a manufacturing example 4 (SUS316-Cr-SPNC), Manufacture Example 5 (SUS316-Cr-Fe-SPNC) and Manufacture Example 6 (SUS316) coated with an immersion carbide layer on the SUS316 coated with a chromium-based coating layer by the pack cementation X-ray diffraction patterns of -Cr-Fe-V-SPNC).
  • Figure 7 is Comparative Example 6 (SUS316-Cr-SPC), Comparative Example 7 (SUS316-Cr-Fe-SPC) and Comparative Example 8 ( X-ray diffraction patterns of SUS316-Cr-Fe-V-SPC).
  • the SUS316 having the carbonaceous layer formed with the screen plasma has a different crystal structure from that of the SUS316 having the carburized layer, and has a different crystal structure depending on the chromium-based material for preparing the coating layer by pack cementation. It confirmed that it represents. As a result, it can be determined that various desired crystal phases can be produced by using pack cementation and screen plasma. In addition, it can be determined that the pack cementation and the screen plasma can be performed together in a process for manufacturing a coating layer on SUS316.
  • a sample having a cross section was prepared by mounting SUJ2 including the coating layer and etching with hydrochloric acid.
  • the cross-sectional shape of the sample was analyzed using an optical microscope and elemental content analysis was performed by glow discharge optical emission spectrometry (GD-OES).
  • FIG. 8 is an image showing the cross-sectional shape of Preparation Example 1 (SUJ2-Cr-SPNC), Figure 9 is a graph showing the element content according to the depth of Preparation Example 1.
  • 10 is an image showing the cross-sectional shape of Preparation Example 2 (SUJ2-Cr-Fe-SPNC), Figure 11 is a graph showing the element content according to the depth of Preparation Example 2.
  • Figure 12 is an image showing the cross-sectional shape of Preparation Example 3 (SUJ2-Cr-Fe-V-SPNC),
  • Figure 13 is a graph showing the element content according to the depth of Preparation Example 3.
  • FIG. 14 is an image showing the cross-sectional shape of Comparative Example 1 (SUJ2-Cr-SPC), Figure 15 is a graph showing the element content of the coating layer of Comparative Example 1.
  • Figure 16 is an image showing the cross-sectional shape of Comparative Example 4 (SUJ2-Cr-Fe-SPC),
  • Figure 17 is a graph showing the element content of the coating layer of Comparative Example 4.
  • Figure 18 is an image showing the cross-sectional shape of Comparative Example 5 (SUJ2-Cr-Fe-V-SPC),
  • Figure 19 is a graph showing the element content of the coating layer of Comparative Example 5.
  • the depth of the chromizing SUJ2 becomes deeper, and the precipitated carbon layer formed by screen plasma or The thickness of the carburized layer may be determined to be about 1 ⁇ m.
  • FIG. 20 is an image showing the cross-sectional shape of Preparation Example 4 (SUS316-Cr-SPNC), Figure 21 is a graph showing the element content according to the depth of Preparation Example 4.
  • 22 is an image showing the cross-sectional shape of Preparation Example 5 (SUS316-Cr-Fe-SPNC), Figure 23 is a graph showing the element content according to the depth of Preparation Example 5.
  • 24 is an image showing the cross-sectional shape of Preparation Example 6 (SUS316-Cr-Fe-V-SPNC), Figure 25 is a graph showing the element content according to the depth of Preparation Example 6.
  • the amount of chromium element was higher than that of other elements, and it was confirmed that the chromium coating layer was present at 60 ⁇ m or more.
  • the vanadium coating layer was present at 70 wt% or more at the outermost surface, and it was confirmed that a coating layer having a uniform content of elements was formed after the depth of 10 ⁇ m from the outermost surface of the coating layer of Preparation Example 5.
  • FIG. 26 is an image showing the cross-sectional shape of Comparative Example 6 (SUS316-Cr-SPC), Figure 27 is a graph showing the element content of the coating layer of Comparative Example 6.
  • Figure 28 is an image showing the cross-sectional shape of Comparative Example 7 (SUS316-Cr-Fe-SPC), Figure 29 is a graph showing the element content of the coating layer of Comparative Example 7.
  • Figure 30 is an image showing the cross-sectional shape of Comparative Example 8 (SUS316-Cr-Fe-V-SPC), Figure 31 is a graph showing the element content of the coating layer of Comparative Example 8.
  • the depth of SUS316 to be chromized becomes deeper, and the precipitated carbon layer formed by screen plasma or The thickness of the carburized layer may be determined to be about 1 ⁇ m.
  • the friction coefficient of the coating layer was a ball-on-disk method for measuring the relative friction coefficient between the product and the hard bearing ball.
  • the ball-on-disk method uses a 6 mm diameter STB 2 ball.
  • a linear velocity of 10 mm / sec and 1N load is used, and the relative humidity is a method of measuring the coefficient of friction in a constant temperature and humidity chamber to maintain a 50% wear condition.
  • FIG. 32 is a graph measuring the coefficient of friction of Preparation Example 1 (SUJ2-Cr-SPNC)
  • Figure 33 is a graph measuring the coefficient of friction of Preparation Example 2 (SUJ2-Cr-Fe-SPNC)
  • Figure 34 is a graph This is a graph measuring the friction coefficient of Example 3 (SUJ2-Cr-Fe-V-SPNC).
  • 35 is a graph measuring the friction coefficient of Comparative Example 1 (SUJ2-Cr-SPC)
  • FIG. 36 is a graph measuring the friction coefficient of Comparative Example 4 (SUJ2-Cr-Fe-SPC)
  • FIG. 37 is a comparison. It is a graph which measured the friction coefficient of Example 5 (SUJ2-Cr-Fe-V-SPC).
  • the coefficient of friction of Preparation Example 1 in which the chromium coating layer and the carbonization layer are present is 0.5
  • the coefficient of friction of Comparative Example 2 in which the chromium coating layer and the carbonization layer is present is 0.6
  • the friction coefficient of Preparation Example 2 in which the chromium-iron coating layer and the precipitated carbonization layer is 0.6 is 0.6
  • the friction coefficient of Comparative Example 4 in which the chromium-iron coating layer and the carbonization layer is present is 0.7.
  • the coefficient of friction of Preparation Example 3 in which the chromium-iron-vanadium coating layer and the precipitated carbonization layer are present is 0.4
  • the coefficient of friction of Comparative Example 5, in which the chromium-iron-vanadium coating layer and the carbide-carburized layer is present is 0.6.
  • SUJ2 which has an impregnated carbonized layer, penetrates nitrogen and carbon in the screen plasma, and penetrates only carbon, thereby lowering the coefficient of friction than SUJ2, which has formed a carburized layer. It can be judged that it is preferable to form an precipitated carbonized layer.
  • FIG. 38 is a graph illustrating a friction coefficient of Comparative Example 2 (SUJ2-SPNC) in which an impregnated carbon layer was formed of screen plasma without performing pack cementation
  • FIG. 39 is carburized with screen plasma without performing pack cementation. It is a graph which measured the friction coefficient of the comparative example 3 (SUJ2-SPC) which formed the flower layer.
  • the SUJ2 having only the screen plasma and the precipitated carbonized layer or the carbonized layer may be determined to have a higher friction coefficient than the SUJ2 having both the pack cementation and the screen plasma.
  • Friction coefficient analysis of SUS316 including a coating layer made of a pack cementation and plasma screen
  • the friction coefficient of the coating layer was a ball-on-disk method for measuring the relative friction coefficient between the product and the high hardness stainless steel ball.
  • the ball-on-disk method uses a 6 mm diameter STS 316 ball.
  • a linear velocity of 10 mm / sec and 1N load is used, and the relative humidity is a method of measuring the coefficient of friction in a constant temperature and humidity chamber to maintain a 50% wear condition.
  • FIG. 40 is a graph measuring the coefficient of friction of Preparation Example 4 (SUS316-Cr-SPNC), Figure 41 is a graph measuring the coefficient of friction of Preparation Example 5 (SUS316-Cr-Fe-SPNC), Figure 42 It is a graph which measured the friction coefficient of Example 6 (SUS316-Cr-Fe-V-SPNC).
  • FIG. 43 is a graph measuring friction coefficient of Comparative Example 6 (SUS316-Cr-SPC)
  • FIG. 44 is a graph measuring friction coefficient of Comparative Example 7 (SUS316-Cr-Fe-SPC)
  • FIG. 45 is a comparison. It is a graph which measured the friction coefficient of Example 8 (SUS316-Cr-Fe-V-SPC).
  • the coefficient of friction of Preparation Example 4 in which the chromium coating layer and the carbonization layer are present is 0.6
  • the coefficient of friction of Comparative Example 6 in which the chromium coating layer and the carbonization layer is present is 0.6.
  • the friction coefficient of Preparation Example 5 in which the chromium-iron coating layer and the precipitated carbonization layer are 0.4 is 0.4
  • the friction coefficient of Comparative Example 7 in which the chromium-iron coating layer and the carbonization layer is present is 0.6.
  • the coefficient of friction of Preparation Example 6 in which the chromium-iron-vanadium coating layer and the precipitated carbonization layer are present is 0.7
  • the coefficient of friction of Comparative Example 8 in which the chromium-iron-vanadium coating layer and the carbonization layer is present is 0.7.
  • Such a result may be determined that the friction coefficient is lowered when the chromium-based material is mixed and coated with the chromium-based material in the pack cementation.
  • SUS316 in which an impregnated carbonization layer is formed by penetrating nitrogen and carbon on the chromium-iron coating layer in a screen plasma infiltrates only carbon, thereby lowering the coefficient of friction than SUS316 in which the carbonization layer is formed. And it can be judged that it is preferable to penetrate all carbon to form an impregnated carbonization layer.
  • Micro Vickers hardness measurement method is a method of measuring the hardness of the material by calculating the size engraved by applying a certain load to the material to be measured with a pyramidal diamond indenter.
  • Table 1 is a table showing the hardness values of the embodiments subjected to the pack cementation and screen plasma using the SUJ2 iron alloy, or the screen plasma only.
  • Hardness was measured using the same method as Experimental Example 7 to analyze the hardness of SUS316 having a coating layer.
  • Table 2 is a table showing the hardness values of the embodiments subjected to the pack cementation and screen plasma using the SUS316 iron-based alloy.
  • the hardness value was higher than 800 HV, which is the hardness value of general SUS316.
  • a chromium-based coating layer and an immersion carbonization layer on an iron-based alloy using pack cementation and screen plasma.
  • the iron-based alloy is used as SUS316
  • the chromated chromium-based coating layer may be formed to a thickness of 60 ⁇ m or more.
  • the friction coefficient of the iron-based alloy formed with the chromium-based coating layer and the precipitated carbonization layer was shown to exhibit a characteristic of lowering to a minimum of 0.4 level, and exhibited improved hardness characteristics of 1450 HV or more.

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Abstract

La présente invention concerne un procédé de revêtement d'un alliage à base de fer et, plus précisément, un procédé de formation d'une couche de revêtement à base de chrome sur une surface d'un alliage à base de fer par cémentation en caisse, et d'une couche nitrocarburée sur la couche de revêtement à base de chrome en utilisant un plasma écran. Ainsi, en utilisant une cémentation en caisse et un plasma écran pour former une couche de revêtement à base de chrome et une couche nitrocarburée sur un alliage à base de fer, la présente invention peut donner un produit ayant une dureté élevée et d'excellentes propriétés à coefficient de frottement réduit.
PCT/KR2017/012944 2016-11-18 2017-11-15 Procédé de revêtement d'un alliage à base de fer et produit ainsi obtenu ayant une dureté élevée et une propriété à coefficient de frottement réduit WO2018093146A1 (fr)

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