CN112708883A - Preparation method of superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating - Google Patents
Preparation method of superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating Download PDFInfo
- Publication number
- CN112708883A CN112708883A CN202011525941.9A CN202011525941A CN112708883A CN 112708883 A CN112708883 A CN 112708883A CN 202011525941 A CN202011525941 A CN 202011525941A CN 112708883 A CN112708883 A CN 112708883A
- Authority
- CN
- China
- Prior art keywords
- boron carbide
- iron
- carbide ceramic
- based alloy
- coating
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- 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
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
- B22F7/04—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
- B22F7/04—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal
- B22F2007/042—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal characterised by the layer forming method
- B22F2007/047—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal characterised by the layer forming method non-pressurised baking of the paste or slurry containing metal powder
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Composite Materials (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Abstract
A preparation method of a superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating comprises the following steps: (1) preparing boron carbide ceramic particles and iron-based self-fluxing alloy powder as raw materials; (2) preparing a steel matrix with a surface to be clad through surface treatment; (3) putting boron carbide ceramic particles and iron-based alloy powder into a ball mill for dry ball milling and mixing; (4) adding a binder into the mixed powder, uniformly stirring to form a viscous paste, and coating the paste on the surface of a steel matrix; (5) drying after air drying; (6) vacuum cladding and furnace cooling. The coating prepared by the method does not have through full-thickness cracks and micro pores, is a continuous closed coating, can obviously improve the wear resistance of mechanical parts, and prolongs the service life and the safety performance.
Description
Technical Field
The invention belongs to the technical field of materials, and particularly relates to a preparation method of a superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating.
Background
Over 50% of the annual consumption of steel materials all over the world is consumed by abrasion and corrosion, 1/3 (total energy) is consumed by friction, and the friction causes the mechanical energy to be converted into internal energy and abrasion, so that parts are failed, and huge economic loss is caused; therefore, the method has great social benefit and economic benefit for improving the wear resistance of the surface of the material. The surface modification technology becomes the focus of research in recent years, and specifically comprises a surface heat treatment technology, a surface alloying technology and a surface coating technology; but the surface strengthening degree of the surface heat treatment and surface alloying technology is limited, and the surface of mechanical parts used in the fields of mining, oil drilling and the like can hardly meet the strict requirement of working conditions; the surface coating technology is based on the principle of metal matrix composite materials, and a firm bonding coating is formed by reacting large-size solid or liquid particles with the surface of a base material under a high-temperature condition, so that the surface coating has flexible and controllable thickness, higher hardness, good wear resistance and the like, and the service life of easily-worn parts in equipment can be greatly prolonged.
The surface coating technology commonly used at present mainly comprises a thermal spraying method, a laser cladding method, a plasma cladding method, an argon arc cladding technology and the like. During thermal spraying, the cooling time of the coating is short, metallurgical bonding is difficult to form between the coating and the substrate, the bonding strength is not high, and microcrack defects are easy to generate, so that the technology can only be applied to working conditions with lower impact and shear stress in the field of wear resistance. In the laser cladding process, because the laser energy is too high, the burning loss and oxidation of the alloy are more serious than those of other technologies, the rapid cooling effect of the liquid phase can also cause the generation of cracks, in addition, the equipment cost is high, the process parameter adjustment is more complex, and the like, and the large-scale industrialization cannot be realized at the current stage. The development of the technology is greatly limited by the defects of low preparation efficiency, high tendency of cracking or peeling of a cladding layer and the like of argon arc cladding. In the plasma cladding technology, a compact coating is difficult to prepare due to the unbalanced forming process of high melting point, high specific heat and rapid heating and cooling, oxidation can occur at high temperature, and the coating cannot be sprayed in the atmosphere generally, but when vacuum spraying is adopted, the ceramic particles cannot be well melted and the compact coating cannot be obtained due to low spraying pressure and low energy density of flame.
In contrast, the vacuum cladding technology is that enough and concentrated heat energy is acted on the coating surface of the base metal under certain vacuum conditions, the coating alloy material which is coated on the surface of the base in advance is melted and infiltrates the surface of the base in a short time, a narrow mutual solution area is formed on an interface through diffusion mutual solution, and then the coating and the mutual solution area are condensed and crystallized together to realize the metallurgical bonding of the coating and the base; the cladding layer formed is generally composed of two phases, an abrasion-resistant reinforcing phase and a binder phase. At present, nickel-based, cobalt-based and iron-based self-fluxing alloy powder is mainly used as a bonding phase, wherein the nickel-based and cobalt-based self-fluxing alloy powder has wide application due to better comprehensive performance; the reinforcing phase mainly comprises oxides, carbides, nitrides and borides, but only the carbides have good wettability with the ferrous metal, so the reinforcing phase is most commonly used, and the research on the wear resistance of the surface of steel reinforced by ceramic particles such as WC, TiC, SiC and the like is most common.
Chinese patent (No. CN 104162676B) proposes a vacuum cladding surface strengthening method for a valve body and a valve seat of a fracturing pump, and a coating with higher density, good wear resistance, corrosion resistance and other properties is obtained by taking nickel-based self-fluxing alloy powder and tungsten carbide ceramic mixed powder as coating materials and carrying out a vacuum cladding process. Chinese patent (No. CN 107675176B) proposes a method for strengthening the surface of a workpiece by combining micro-arc oxidation and vacuum cladding, which comprises preparing a thin layer of aluminum (the main component of which is crystalline alpha-Al) on the surface of the workpiece by a hot-dip aluminum plating method2O3And gamma-Al2O3) And preparing a high-hardness wear-resistant ceramic coating on the aluminum-based film layer by using micro-arc oxidation, and then sealing micropores on the surface of the ceramic layer by using vacuum cladding Ni60A powder to form a compact coating. Chinese patent (application No. 201910898914.7) proposes a structure of vacuum cladding, chemical plating and melting-plating composite coating and a preparation method thereof, combines the vacuum cladding technology and the chemical plating technology, and prepares the tungsten carbide cladding and the graphene oxide cladding as composite layers to obtain the melting-plating composite coating with comprehensive functions. Currently, the preparation of the coating by using a vacuum cladding technology is mostly focused on the combination of nickel-based and tungsten carbide and composite cladding by combining other cladding technologies to further strengthen the performance of the coating, but the preparation process is more complex, and the used nickel-based and cobalt-based alloy powder has good comprehensive performance but is expensive and not suitable for large-scale preparation.
Disclosure of Invention
The invention aims to provide a preparation method of a superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating, which adopts a vacuum cladding method to prepare the composite wear-resistant coating, overcomes the defects of low bonding strength, large residual stress and the like of the composite coating prepared by methods such as thermal spraying, laser cladding and the like, meanwhile, a boron carbide superhard ceramic phase is introduced as a reinforcing phase, and a composite coating consisting of an iron-nickel solid solution, incompletely decomposed boron carbide and various eutectic compounds (chromium-rich and iron-rich carborides) is obtained through regulation and control of process, components and structure, the formed iron-nickel solid solution is used as a coating substrate, has certain binding and supporting functions on undecomposed boron carbide, newly formed chromium-rich and iron-rich carborides and other hard phases, so that the hard phase is not easy to fall off in the abrasion process, the grinding surface is protected, and the abrasion resistance of the coating is greatly improved.
The method comprises the following steps:
1. preparing boron carbide ceramic particles and iron-based self-fluxing alloy powder as raw materials; the particle size of the boron carbide ceramic particles is 10-40 mu m, and the particle size of the iron-based alloy powder is 40-100 mu m; the iron-based self-fluxing alloy is Fe60 self-fluxing alloy or Fe-Cr-C alloy;
2. preparing a steel matrix with a surface to be clad through surface treatment;
3. putting the boron carbide ceramic particles and the iron-based alloy powder into a ball mill for dry ball milling and mixing, wherein the ball milling and mixing time is 3-6 h, and the ball milling rotation speed is 300-500 rpm, so as to obtain mixed powder; the mass of the boron carbide ceramic particles accounts for 5-30% of the total mass of the boron carbide ceramic particles and the iron-based alloy powder during ball milling and mixing;
4. adding a binder into the mixed powder, uniformly stirring to form a viscous paste, coating the paste on the surface of a steel matrix, and obtaining a prefabricated coating on the surface of the steel matrix;
5. air-drying the steel substrate with the pre-coating, and then drying to volatilize the binder, thereby obtaining a pre-coated steel substrate with a coating precursor;
6. and placing the pre-coated steel matrix in a vacuum furnace for vacuum cladding, then cooling to normal temperature along with the furnace, and obtaining the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating on the surface of the steel matrix.
In the step 2, the surface treatment step is: mechanically polishing the surface to be clad of the steel matrix material, then removing oxide by acid washing, wiping the surface with organic solvent alcohol or acetone to remove oil stain on the surface, and finally drying to remove the organic solvent.
In the step 3, the ball-material ratio during ball milling and mixing is 2-3.
In the step 4, the binder is selected from water glass, polyethylene glycol, absolute ethyl alcohol or saturated rosin solution.
In the step 4, the thickness of the prefabricated coating is 1-4 mm.
In the step 5, the air drying temperature is room temperature, and the air drying time is 12-24 hours.
In the step 5, the drying temperature is 100-200 ℃ and the drying time is 3-6 h.
In the step 6, when vacuum cladding is performed, the pressure in the vacuum furnace is controlled to be less than or equal to 5 multiplied by 10-2Pa; firstly, heating a pre-coated steel substrate to 300-400 ℃, and preserving heat for 30-60 min to ensure that the residual binder is completely volatilized; and then heating to the melting point temperature of the iron-based alloy powder to enable the coating precursor on the steel matrix to be in a molten state, and preserving heat for 20-60 min to complete vacuum cladding.
The boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is metallurgically bonded with a steel substrate to form a bonding interface; the thickness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 1-4 mm.
The matrix of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is an iron-nickel solid solution, and the reinforcing phase is incompletely decomposed boron carbide and an eutectic compound; the eutectic compound comprises a chromium-rich carborundum compound and an iron-rich carborundum compound.
The microhardness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 500-1300 HV.
In the technical field of wear-resistant coatings, compared with the prior art, the iron-based alloy powder has wide sources and low cost, is similar to the components of a steel matrix, and is easy to form firm metallurgical bonding with a steel substrate, so the iron-based alloy powder has wide application prospect; the boron carbide ceramic particles have the third highest hardness in nature, are second to diamond and cubic boron nitride, have the characteristics of high wear resistance and good self-lubricating property, play an important role in the industries of hard alloy and coating, and are commonly used for manufacturing wear-resistant parts. The method can clad the boron carbide ceramic particles with high melting point and high hardness on the surface of the steel material without high temperature treatment, construct the composite wear-resistant coating which takes the iron-nickel solid solution as the coating matrix and takes the incompletely decomposed boron carbide ceramic particles and a plurality of hard phases such as chromium-rich and nickel-rich carborides as the reinforcing phases, fully play the 'supporting effect' of the coating matrix and the 'shadow effect' of the reinforcing phases, ensure that the composite coating has excellent cutting resistance and adhesion wear resistance, and has important significance for expanding the application of universal steel material wear-resistant parts.
The method of the invention prepares a reasonable compounding process by a vacuum cladding technology, fully exerts the characteristics of high hardness and high wear resistance of boron carbide ceramic particles and the obvious cost performance advantage of iron-based alloy powder, fully ball-mills the boron carbide ceramic particles and the iron-based alloy powder in a proper proportion to homogenize and alloy the boron carbide ceramic particles, uniformly stirs the boron carbide ceramic particles and the iron-based alloy powder by using an organic solvent which is pollution-free and has no harmful phase, coats the boron carbide ceramic particles on the surface of steel materials under different working conditions, the coating thickness depends on the requirements of actual working conditions, and finally carries out cladding forming according to a cladding process in a high vacuum environment to finally prepare a composite wear-resistant coating taking an iron-nickel solid solution as a coating matrix, wherein a plurality of carbide-boride hard phases and unde.
Compared with the existing thermal spraying, laser cladding, plasma cladding and argon arc cladding technologies and vacuum cladding technologies, the prepared coating does not have cracks and micro pores penetrating through the whole thickness, is a continuous closed coating, and has better antirust and corrosion resistant performance than an electroplated layer and a thermal sprayed coating; the thickness range of the coating is wide and can be controlled according to specific working conditions, the thick coating can bear larger impact load, and the coating is not easy to break; the components of the coating can be freely adjusted according to the requirements, and the microhardness of the coating is difficult to achieve by other coating processes; the structure of the coating is uniform, the hardness distribution is uniform, and the phenomena of component segregation, nonuniform structure, lapping among molten pools, nonuniform coating hardness and the like in the molten pools can be generated unlike laser beam melting, electron beam melting, focused beam melting and plasma beam melting; meanwhile, the composite wear-resistant coating prepared under the high vacuum condition has no oxidation phenomenon, so that the performance of the prepared composite wear-resistant coating is more stable; the method of the invention can obviously improve the wear resistance of mechanical parts and greatly prolong the service life and the safety performance.
Drawings
FIG. 1 is a schematic flow diagram of the present invention;
fig. 2 is a photograph showing the appearance of the boron carbide ceramic particle-reinforced iron-based alloy composite wear-resistant coating prepared in example 1 before and after processing, wherein the upper drawing is before processing, and the lower drawing is after processing;
FIG. 3 is a metallographic structure diagram of a boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating prepared in example 1 of the present invention;
FIG. 4 is a graph showing hardness distributions of a boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating, a bonding interface and a steel matrix prepared in example 1 of the present invention;
fig. 5 is an abrasion microstructure diagram of the abrasive particles of the boron carbide ceramic particle reinforced iron-based alloy composite abrasion-resistant coating prepared in example 1 of the invention.
Detailed Description
The boron carbide ceramic particles adopted in the embodiment of the invention are commercial products.
The Fe60 (iron-based) self-fluxing alloy powder used in the examples of the present invention is a commercially available product.
The Fe-Cr-C alloy powder adopted in the embodiment of the invention is FeCr55C6.0 alloy powder or FeCr67C9.5 alloy powder.
The ball mill in the embodiment of the invention is a planetary ball mill.
The alcohol and acetone in the examples of the present invention are commercially available industrial grade products.
The water glass, the polyethylene glycol, the absolute ethyl alcohol and the saturated rosin solution in the embodiment of the invention are commercially available products.
The surface treatment in the embodiment of the invention comprises the following steps: mechanically polishing the surface to be clad of the steel matrix material, then removing oxide by acid washing, wiping the surface with organic solvent alcohol or acetone to remove oil stain on the surface, and finally drying to remove the organic solvent.
In the embodiment of the invention, the thickness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 1-4 mm.
In the embodiment of the invention, the material of the steel substrate is 304 stainless steel or 45# steel.
In the embodiment of the invention, the air drying temperature is room temperature, and the air drying time is 12-24 h.
In the embodiment of the invention, the drying temperature is 100-200 ℃ and the drying time is 3-6 h.
Example 1
The flow is shown in figure 1;
preparing boron carbide ceramic particles and iron-based self-fluxing alloy powder as raw materials; the particle size of the boron carbide ceramic particles is 10-40 mu m, and the particle size of the iron-based alloy powder is 40-100 mu m; the iron-based self-fluxing alloy is FeCrBSi (Fe60) self-fluxing alloy;
preparing a 45# steel substrate with the size of 60mm multiplied by 10mm, and forming a surface to be clad through surface treatment;
putting the boron carbide ceramic particles and the iron-based alloy powder into a ball mill for dry ball milling and mixing, wherein the ball-material ratio during ball milling and mixing is 2, the ball milling and mixing time is 6h, and the ball milling rotating speed is 300rpm, so as to obtain mixed powder; the mass of the boron carbide ceramic particles accounts for 10% of the total mass of the boron carbide ceramic particles and the iron-based alloy powder during ball milling and mixing;
adding a binder into the mixed powder, uniformly stirring to form a viscous paste, coating the paste on the surface of a steel matrix, and obtaining a prefabricated coating with the thickness of 1mm on the surface of the steel matrix; the binder is a saturated rosin solution;
air-drying the steel substrate with the pre-coating, and then drying to volatilize the binder, thereby obtaining a pre-coated steel substrate with a coating precursor;
putting the pre-coated steel substrate into a vacuum furnace for vacuum cladding, and controlling the pressure in the vacuum furnace to be less than or equal to 5 multiplied by 10 during the vacuum cladding-2Pa; firstly, heating a precoated steel substrate to 300 ℃, and preserving heat for 60min to ensure that residual binder is completely volatilized, prevent the formation of more and larger air hole defects due to volatilization in the high-temperature cladding process, and avoid influencing the density of a coating and the wear resistance of a product; then heating to the melting point temperature of the iron-based alloy powder to enable the coating precursor on the steel matrix to be in a molten state, and preserving heat for 60 min; after vacuum cladding is finished, cooling the steel substrate to normal temperature along with the furnace, and obtaining the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating on the surface of the steel substrate;
the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is metallurgically bonded with a steel substrate to form a bonding interface; the matrix of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is an iron-nickel solid solution, and the reinforcing phase is incompletely decomposed boron carbide and an eutectic compound; the eutectic compound comprises a chromium-rich carborundum compound and an iron-rich carborundum compound;
the appearance of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating before and after processing is shown in figure 2; the microstructure of the coating part and the substrate is shown in figure 3, the coating and the substrate show good metallurgical bonding, and the interface bonding strength is very good; the micro-hardness distribution curves of the coating part and the matrix are shown in figure 4, the micro-hardness of the coating is far higher than that of the steel matrix, and the micro-hardness of the coating is greatly improved by the aid of the incompletely decomposed boron carbide and newly formed chromium-rich and iron-rich carborundum and other reinforcing phases in the composite coating, and the micro-hardness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 500-1300 HV; the wear surface appearance of the coating after a high stress abrasive particle wear test is shown in fig. 5, and thick massive reinforcing phases and thick strip reinforcing phases are distributed in a coating substrate and are used as a wear-resistant framework to form firm metallurgical bonding with the coating iron-nickel solid solution substrate, so that the cutting resistance and the adhesion wear resistance are improved, and the overall wear resistance of the cladding layer is enhanced.
Example 2
The method is the same as example 1, except that:
(1) the iron-based self-fluxing alloy is Fe-Cr-C alloy;
(2) the substrate is 304 stainless steel substrate with the size
(3) The ball-material ratio during ball milling and mixing is 3, the time is 3h, and the rotating speed is 500 rpm; the mass of the boron carbide ceramic particles accounts for 20% of the total mass of the boron carbide ceramic particles and the iron-based alloy powder;
(4) the thickness of the prefabricated coating is 2 mm; the binder is absolute ethyl alcohol;
(5) heating to 400 ℃ during vacuum cladding, and keeping the temperature for 30 min; then heating to the melting point temperature of the iron-based alloy powder, and keeping the temperature for 50 min;
the microhardness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 500-1300 HV.
Example 3
The method is the same as example 1, except that:
(1) the ball-material ratio during ball milling and mixing is 2.5, the time is 4h, and the rotating speed is 400 rpm; the mass of the boron carbide ceramic particles accounts for 5% of the total mass of the boron carbide ceramic particles and the iron-based alloy powder;
(2) the thickness of the prefabricated coating is 3 mm; the binder is water glass;
(3) heating to 350 deg.C during vacuum cladding, and maintaining for 40 min; then heating to the melting point temperature of the iron-based alloy powder, and preserving heat for 40 min;
the microhardness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 500-1300 HV.
Example 4
The method is the same as example 1, except that:
(1) the iron-based self-fluxing alloy is Fe-Cr-C alloy;
(2) the substrate is a 304 stainless steel substrate;
(3) the ball-material ratio during ball milling and mixing is 2.5, the time is 5h, and the rotating speed is 350 rpm; the mass of the boron carbide ceramic particles accounts for 30% of the total mass of the boron carbide ceramic particles and the iron-based alloy powder;
(4) the thickness of the prefabricated coating is 4 mm; the binder is polyethylene glycol;
(5) heating to 350 deg.C during vacuum cladding, and maintaining for 50 min; then heating to the melting point temperature of the iron-based alloy powder, and keeping the temperature for 30 min;
the microhardness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 500-1300 HV.
Claims (8)
1. A preparation method of a superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating is characterized by comprising the following steps:
(1) preparing boron carbide ceramic particles and iron-based self-fluxing alloy powder as raw materials; the particle size of the boron carbide ceramic particles is 10-40 mu m, and the particle size of the iron-based alloy powder is 40-100 mu m; the iron-based self-fluxing alloy is Fe60 self-fluxing alloy or Fe-Cr-C alloy;
(2) preparing a steel matrix with a surface to be clad through surface treatment;
(3) putting the boron carbide ceramic particles and the iron-based alloy powder into a ball mill for dry ball milling and mixing, wherein the ball milling and mixing time is 3-6 h, and the ball milling rotation speed is 300-500 rpm, so as to obtain mixed powder; the mass of the boron carbide ceramic particles accounts for 5-30% of the total mass of the boron carbide ceramic particles and the iron-based alloy powder during ball milling and mixing;
(4) adding a binder into the mixed powder, uniformly stirring to form a viscous paste, coating the paste on the surface of a steel matrix, and obtaining a prefabricated coating on the surface of the steel matrix;
(5) air-drying the steel substrate with the pre-coating, and then drying to volatilize the binder, thereby obtaining a pre-coated steel substrate with a coating precursor;
(6) and placing the pre-coated steel matrix in a vacuum furnace for vacuum cladding, then cooling to normal temperature along with the furnace, and obtaining the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating on the surface of the steel matrix.
2. The method for preparing the superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein in the step (3), the ball-to-material ratio during ball milling and mixing is 2-3.
3. The method for preparing the superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein in the step (4), the binder is selected from water glass, polyethylene glycol, absolute ethyl alcohol or saturated rosin solution.
4. The method for preparing the superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein in the step (4), the thickness of the prefabricated coating is 1-4 mm.
5. The method for preparing the superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein in the step (6), the pressure in a vacuum furnace is controlled to be less than or equal to 5 x 10 during vacuum cladding-2Pa; firstly, heating a pre-coated steel substrate to 300-400 ℃, and preserving heat for 30-60 min to ensure that the residual binder is completely volatilized; and then heating to the melting point temperature of the iron-based alloy powder to enable the coating precursor on the steel matrix to be in a molten state, and preserving heat for 20-60 min to complete vacuum cladding.
6. The method for preparing a superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein the boron carbide ceramic particles are metallurgically bonded with the iron-based alloy composite wear-resistant coating and a steel substrate to form a bonding interface; the thickness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 1-4 mm.
7. The method for preparing the superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein the matrix of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is an iron-nickel solid solution, and the reinforcing phase is incompletely decomposed boron carbide and a eutectic compound; the eutectic compound comprises a chromium-rich carborundum compound and an iron-rich carborundum compound.
8. The method for preparing the superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating according to claim 1, wherein the microhardness of the boron carbide ceramic particle reinforced iron-based alloy composite wear-resistant coating is 500-1300 HV.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011525941.9A CN112708883B (en) | 2020-12-22 | 2020-12-22 | Preparation method of superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011525941.9A CN112708883B (en) | 2020-12-22 | 2020-12-22 | Preparation method of superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112708883A true CN112708883A (en) | 2021-04-27 |
| CN112708883B CN112708883B (en) | 2022-03-22 |
Family
ID=75544993
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011525941.9A Active CN112708883B (en) | 2020-12-22 | 2020-12-22 | Preparation method of superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112708883B (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113373439A (en) * | 2021-05-28 | 2021-09-10 | 西安科技大学 | Composite coating for improving surface wear resistance of 35CrMoV steel and preparation method thereof |
| CN114774907A (en) * | 2022-04-28 | 2022-07-22 | 太原理工大学 | Preparation method of nano diamond particle enhanced wear-resistant coating on titanium alloy surface |
| CN114798378A (en) * | 2022-04-25 | 2022-07-29 | 亳州市亚珠新材料有限公司 | Carbon sheet and aluminum-silicon composite material thereof |
| CN114985728A (en) * | 2022-06-09 | 2022-09-02 | 海南大学 | Ceramic/iron-based composite coating, carbon steel-based composite material and preparation method thereof |
| CN115011961A (en) * | 2022-06-14 | 2022-09-06 | 绍兴文理学院 | Manufacturing process of self-lubricating wear-resistant coating of hob |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1609274A (en) * | 2004-09-16 | 2005-04-27 | 北京科技大学 | Carbonide / iron-base alloy composite coating and its reaction brass coating technology |
| EP1967601A2 (en) * | 2007-03-06 | 2008-09-10 | Bayerische Motoren Werke Aktiengesellschaft | Method for manufacturing a coating |
| CN104162676A (en) * | 2014-07-25 | 2014-11-26 | 北京科技大学 | Fracturing pump valve body and valve seat vacuum fusion covering surface strengthening method |
| CN107630215A (en) * | 2017-08-21 | 2018-01-26 | 陕西天元智能再制造股份有限公司 | A kind of wear resistant corrosion resistant processing method of workpiece surface |
| CN109023345A (en) * | 2018-08-08 | 2018-12-18 | 天津德天助非晶纳米科技有限公司 | Ternary boride reinforced iron-base wear-resistant coating and preparation method thereof |
-
2020
- 2020-12-22 CN CN202011525941.9A patent/CN112708883B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1609274A (en) * | 2004-09-16 | 2005-04-27 | 北京科技大学 | Carbonide / iron-base alloy composite coating and its reaction brass coating technology |
| EP1967601A2 (en) * | 2007-03-06 | 2008-09-10 | Bayerische Motoren Werke Aktiengesellschaft | Method for manufacturing a coating |
| CN104162676A (en) * | 2014-07-25 | 2014-11-26 | 北京科技大学 | Fracturing pump valve body and valve seat vacuum fusion covering surface strengthening method |
| CN107630215A (en) * | 2017-08-21 | 2018-01-26 | 陕西天元智能再制造股份有限公司 | A kind of wear resistant corrosion resistant processing method of workpiece surface |
| CN109023345A (en) * | 2018-08-08 | 2018-12-18 | 天津德天助非晶纳米科技有限公司 | Ternary boride reinforced iron-base wear-resistant coating and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 崔泽琴 等: "碳钢表面激光熔覆铁基B4C陶瓷涂层的组织与性能", 《材料热处理学报》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113373439A (en) * | 2021-05-28 | 2021-09-10 | 西安科技大学 | Composite coating for improving surface wear resistance of 35CrMoV steel and preparation method thereof |
| CN113373439B (en) * | 2021-05-28 | 2022-12-13 | 西安科技大学 | Composite coating for improving surface wear resistance of 35CrMoV steel and preparation method thereof |
| CN114798378A (en) * | 2022-04-25 | 2022-07-29 | 亳州市亚珠新材料有限公司 | Carbon sheet and aluminum-silicon composite material thereof |
| CN114774907A (en) * | 2022-04-28 | 2022-07-22 | 太原理工大学 | Preparation method of nano diamond particle enhanced wear-resistant coating on titanium alloy surface |
| CN114985728A (en) * | 2022-06-09 | 2022-09-02 | 海南大学 | Ceramic/iron-based composite coating, carbon steel-based composite material and preparation method thereof |
| CN114985728B (en) * | 2022-06-09 | 2024-05-14 | 海南大学 | Ceramic/iron-based composite coating, carbon steel-based composite material and preparation methods thereof |
| CN115011961A (en) * | 2022-06-14 | 2022-09-06 | 绍兴文理学院 | Manufacturing process of self-lubricating wear-resistant coating of hob |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112708883B (en) | 2022-03-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112708883B (en) | Preparation method of superhard boron carbide ceramic reinforced iron-based alloy composite wear-resistant coating | |
| CN104018156B (en) | A kind of Metal Substrate/diamond laser composite coating and preparation method thereof | |
| CN104404434B (en) | A kind of ceramic coating of metal material surface and preparation method thereof | |
| Sun et al. | Research progress in surface strengthening technology of carbide-based coating | |
| CN111334743B (en) | Preparation method of zirconium boride-zirconium carbide-silicon carbide composite coating | |
| CN106119762B (en) | A kind of boride cement coating material and preparation method | |
| CN111235511B (en) | Preparation method of multi-element ceramic composite coating | |
| CN105648386A (en) | Thermal spraying aluminum oxide-yttrium oxide composite ceramic coating and preparing method thereof | |
| CN102154609A (en) | Preparation method of high-precision roller wear-resistant coating | |
| CN110117788A (en) | A kind of preparation method of CoCrFeMnNi high-entropy alloy cladding layer | |
| CN110079756A (en) | A kind of preparation method of chromium carbide wear-resistant coating | |
| CN112063951A (en) | Magnesium-aluminum alloy surface laser cladding self-lubricating coating and construction method thereof | |
| CN103484814A (en) | Preparation method of titanium boride based inorganic composite coating | |
| CN113151772A (en) | Novel high-temperature corrosion-resistant thermal barrier coating with double ceramic layer structure and preparation method thereof | |
| CN112974813B (en) | Titanium-based composite powder and preparation method thereof, in-situ reinforced titanium-based composite coating and preparation method thereof | |
| CN105603352A (en) | Al2O3/YAG amorphous/eutectic composite ceramic coating and preparation method thereof | |
| CN105401116A (en) | Preparation method for titanium alloy TiAl3-Al composite coating | |
| CN106011840A (en) | Impact-resistant metal ceramic wear-resistant coating and preparation method thereof | |
| CN104789961B (en) | A kind of wear-resistant bucket tooth and plasma cladding method with multiple dimensioned hardening constituent coating | |
| CN107523778A (en) | The preparation method of hafnium boride composite coating | |
| CN113355625A (en) | NbC-reinforced high-entropy alloy-based composite coating and preparation method thereof | |
| CN111334742A (en) | Method for preparing ceramic composite coating of refractory transition metal compound | |
| CN105296909A (en) | Galvanizing zinc corrosion resistant boride and method for preparing metal ceramic gradient coatings | |
| CN104446397B (en) | A kind of hard alloy sub-micron crystal ceramic coating and preparation method | |
| CN113278960B (en) | Novel plasma surfacing Fe-Mo 2 FeB 2 Method for producing a transition layer |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |