CN118600359A - Nano TiC-Al2O3Composite coating and preparation method thereof - Google Patents
Nano TiC-Al2O3Composite coating and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a nano TiC-Al 2O3 composite coating and a preparation method thereof, belonging to the field of high-energy beam surface treatment and surface protection. The method takes micron-sized graphite (or carbon black) powder, titanium powder, tiO 2 powder and metal Al powder as raw materials, and comprises the following steps: oil removal and sand blasting treatment are carried out on the surface of the matrix sample; mechanically mixing the Ti-C agglomerated powder subjected to spray granulation and the TiO 2 -Al-C agglomerated powder according to a certain proportion to obtain spray composite powder; pre-spraying a Ni/Al bonding layer with the thickness of 60-100 mu m on the surface of the sandblasted matrix by adopting a plasma spraying technology; the sprayed composite powder is sent into a self-propagating reaction between high-temperature plasma flame flows Ti and C, an aluminothermic reaction and a carbothermic reduction reaction among TiO 2, al and C, tiC and Al 2O3 products are synthesized in situ, and after rapid solidification and crystallization, the nano TiC-Al 2O3 composite coating with good combination, fine crystal grain (submicron or even nanometer level), high compactness and thickness of 300-450 μm is obtained. By adjusting the proportion of the Ti-C agglomerated powder and the TiO 2 -Al-C agglomerated powder in the composite powder, particularly the proportion of Ti/C and TiO 2/Al/C in the agglomerated powder, the controllable preparation of reaction products in the spraying process can be basically realized, the regulation and control of the structure of the composite coating can be realized, the composite coating with different performances can be obtained, and the application range of TiC, al 2O3 and composite materials or coatings thereof can be widened.
Description
Technical Field
The invention belongs to the field of high-energy beam surface treatment, and particularly relates to a nano TiC-Al 2O3 composite coating and a preparation method thereof.
Background
With the continuous development of the technology in the industrial field, the working environment of parts becomes worse, so that the base material cannot meet the use requirements in the environments of friction and abrasion, corrosion, high temperature and the like. The surface coating technology can obviously improve or endow the base material with better performances of wear resistance, corrosion resistance, high temperature resistance and the like.
Titanium carbide (TiC) is a typical transition metal carbide, has excellent properties such as high hardness (28 GPa or more), high melting point (3140 ℃) and high elastic modulus, stable chemical properties, and good wear resistance, high-temperature strength and ablation resistance, and has remarkable advantages in protecting parts from wear and corrosion as a coating. TiC thin films (8-15 μm) prepared by physical vapor deposition and chemical vapor deposition have been successfully applied to various wear resistant parts (such as tools, dies, mechanical parts, etc.), but they are limited by low deposition efficiency and high cost. The thick coating has better wear-resistant protection effect and comprehensive performance in extreme environments such as high load, high speed, long service time and the like. Among the preparation methods of the coating, the plasma spraying technology is widely applied and expected because of the advantages of simple process, flexibility, convenience, high deposition efficiency, capability of realizing large-area thick coating preparation (more than 300 mu m and even up to 1 mm), wide sprayable materials, no influence on matrix tissues and the like.
When the TiC coating is prepared by directly spraying high-melting-point TiC powder by plasma, the problems of insufficient melting and easy oxidation are easy to occur, and the prepared TiC coating is low in density and high in brittleness. In addition, tiC is a ceramic material mainly having a covalent bond, and is inherently brittle. For this reason, a single TiC coating is rarely applied. Compared with a single TiC coating, the TiC composite coating prepared by the second phase (metal or ceramic) can not only exert high strength and high hardness of TiC ceramic, but also improve fracture toughness and compactness of TiC ceramic. However, when the TiC composite coating is prepared by directly adding the second phase, the coating phase interface is easy to pollute, the density and the bonding strength are reduced, and particularly when the nanometer second phase is added, the preparation cost is high, and the crystal grains are easy to grow and agglomerate at high temperature, so that a crack source is deformed.
Based on the above situation, the invention uses the plasma spraying technology, takes cheap micron-sized graphite (or carbon black), titanium powder, tiO 2 and metal Al powder as raw materials, utilizes high-temperature plasma flame flow to ignite self-propagating reaction, aluminothermic reaction and carbothermic reduction reaction among the raw materials to synthesize TiC and Al 2O3 products in situ, and simultaneously, the products are rapidly solidified and crystallized to obtain nanocrystalline after impacting the surface of a substrate under the dragging action of high-speed flame flow, thus preparing the nano TiC-Al 2O3 composite coating with excellent comprehensive mechanical properties (such as good fracture toughness, high compactness and good bonding strength) and thickness of over 300 mu m. In view of this, the present invention has been made.
Disclosure of Invention
The invention aims to provide a preparation method of a nano TiC-Al 2O3 composite coating, aiming at the problems that a single TiC coating is large in brittleness and insufficient in compactness, a second phase is additionally added to pollute a coating interface, the coating performance is deteriorated and the like. The method comprises the steps of respectively obtaining agglomerated Ti-C powder and TiO 2 -Al-C powder through spray granulation, mixing the agglomerated powder with two different proportions through mechanical stirring, and spraying as spraying composite powder. The invention utilizes high-temperature plasma flame flow to ignite aluminothermic and carbothermic reduction reaction, synthesizes TiC and Al 2O3 products in situ and rapidly solidifies and crystallizes to obtain the nano TiC-Al 2O3 composite coating with good combination, fine crystal grain and high compactness, fully exerts the excellent characteristics of TiC and Al 2O3, and ensures that the composite coating is used for abrasion under high-speed and high-load conditions.
In order to achieve the above purpose, the technical scheme of the invention is realized as follows:
A nano TiC-Al 2O3 composite coating and a preparation method thereof comprise the following steps:
step 1, oil removal and sand blasting treatment are carried out on the surface of a matrix sample, wherein the matrix material is metal or ceramic;
Step 2, taking micron-sized Ti powder and graphite (or carbon black) as raw materials, carrying out high-speed centrifugal atomization, drying and collecting to obtain Ti-C agglomerated powder, sieving to obtain Ti-C agglomerated powder with the granularity of 38-74 mu m, and carrying out spray granulation to prepare TiO 2 -Al-C agglomerated powder with the granularity of 40-74 mu m by taking micron-sized graphite (or carbon black), tiO 2 and metal Al powder as raw materials;
Step3, mechanically stirring and mixing TiO 2 -Al-C agglomerated powder and Ti-C agglomerated powder in different proportions to obtain spraying composite powder;
Step 4, spraying pre-spraying Ni/Al self-fluxing alloy powder on the surface of the substrate after sand blasting in a plasma mode, and preparing a Ni/Al bonding layer with the thickness of 60-100 mu m;
Step 5, the spraying composite powder is sent into a plasma flame flow by utilizing a powder sending device, based on self-propagating reaction between Gao Wenyan flows of Ti and C, the thermit reaction and carbothermic reaction between TiO 2, al and C are carried out, tiC and Al 2O3 products are synthesized in situ and rapidly deposited on the surface of a Ni/Al bonding layer, and a nano TiC-Al 2O3 composite coating with the thickness of 300-450 mu m is obtained after solidification and crystallization;
In the step 1, the metal matrix is carbon steel, alloy steel, aluminum alloy, titanium alloy and the like.
In the step 1, corundum sand or silicon carbide sand is adopted for the matrix roughening treatment.
The grain size of Ti powder used in the step 2 is 10-48 mu m, the grain size of graphite (or carbon black) is 1-5 mu m, the grain size of Al powder is 5-10 mu m, and the grain size of TiO 2 is 10-30 mu m.
The mass of graphite (or carbon black) used in the spray granulation process in the step 2 is 10-20% of the mass of Ti powder.
And (2) after spray granulation, drying and collection, selecting a 100-300 mesh round hole mesh screen for sieving.
The mass of the mechanically stirred TiO 2 -Al-C agglomerated powder in the step 3 is 0-30% of the mass of the Ti-C agglomerated powder.
The self-fluxing alloy powder sprayed in the step 4 is 90wt.% of Ni-Al alloy powder, and the granularity is 40-70 mu m.
The spraying angle in the step 5 is 90 degrees, the spraying power is 25-40 kW, and the spraying distance is 80-120 mm.
The plasma gas and the powder feeding gas used in the step 5 are argon, the flow is 20-50L/min and 2-5L/min respectively, and the pressure is 0.6-0.8 MPa.
In the step5, hydrogen is used as combustion gas, the flow is 5-15L/min, and the pressure is 0.6-0.8 MPa.
The nano TiC-Al 2O3 composite coating prepared by the process fully utilizes the high strength, high hardness and high temperature stability of TiC and Al 2O3, and the in-situ synthesized TiC and Al 2O3 are rapidly solidified and formed into the ultra-thick TiC-Al 2O3 composite coating with fine crystal grains, clean interface, high density and excellent comprehensive performance under the dragging action of high-speed plasma flame flow after impacting the surface of a substrate at a high speed.
Compared with the prior art, the invention has the following advantages:
(1) The invention uses spray granulation to gather Ti powder, graphite (carbon black), tiO 2 powder and metal Al powder into Ti-C agglomerate powder and TiO 2 -Al-C agglomerate powder with high sphericity and good fluidity, which can be directly used for plasma spraying after sieving, thereby avoiding the limitation of the coating preparation technology to the shape, size and variety of raw materials and expanding the application field of powder;
(2) In the invention, graphite (carbon black), titanium powder, tiO 2 powder and metal Al powder which are low in price are used as raw materials, and high-temperature flame flow is used for igniting Ti and C to react, and TiO 2, al and C are subjected to aluminothermic reaction and carbothermic reduction reaction to synthesize TiC and Al 2O3 products in situ. The TiC-Al 2O3 composite coating with fine crystal grains (submicron or even nanometer level), crystallized interface, uniform distribution and high density is obtained by rapid solidification and crystallization after the product impacts the bonding layer, so that the problems of interface pollution, poor dispersibility, low bonding strength and the like of the composite coating prepared by externally adding the ceramic phase can be solved, the preparation cost is greatly reduced, and the preparation period of the carbide material is shortened;
(3) Al 2O3 and TiC formed by in-situ reaction are synchronously deposited on the surface of the bonding layer, and are mutually restrained in the rapid solidification process, so that fine Al 2O3 particles are obtained and are dispersed around the TiC particles, lamellar gaps and holes of the plasma spraying coating are effectively filled, the density and the bonding strength of the coating are greatly improved, and a composite coating with excellent comprehensive performance is obtained;
(4) Because Al 2O3 has excellent high-temperature stability and oxidation resistance, when being used as an enhancement phase to be distributed around TiC, the coating can not only improve the heat resistance of the coating, but also be used as a hard phase to relieve stress concentration in the friction and wear process, reduce crack initiation and improve the wear resistance of the coating;
(5) The composite coating prepared by the process of the invention takes TiC and Al 2O3 as main phases, a small amount of TiO x and residual Al phases, and has simple process, short preparation period and low cost, thus obtaining the wear-resistant and heat-resistant coating. Compared with the single TiC coating prepared by plasma spraying, the TiC-Al 2O3 composite coating prepared by the method has the porosity reduced from 11.9% to 7.5%; compared with a single TiC coating, the wear rate of the coating is reduced from 6 multiplied by 10 -3mm3 to 2.7 multiplied by 10 -3mm3 under the same friction experiment condition, the friction coefficient is reduced from 0.54 to 0.43, namely the wear rate and the friction coefficient are respectively reduced by about 55 percent and 20 percent, and the wear resistance is obviously improved;
(6) In the plasma spraying process, ti-C agglomerated powder and TiO 2 -Al-C agglomerated powder are taken as independent reaction units, are fed into high-temperature flame flow through a powder feeding device to ignite Ti-C reaction, and after TiO 2, al-C aluminothermic reaction and carbothermic reaction, a large amount of heat is generated to overlap plasma flame flow to mutually promote the self-propagating reaction, so that a composite coating with sufficient reaction, high compactness and good combination is obtained;
(7) The TiC-Al 2O3 composite coating sprayed by the plasma has excellent performances of high hardness, high strength, wear resistance, heat resistance and corrosion resistance, and is suitable for being applied to the surfaces of workpieces in working conditions such as abrasion, corrosion and the like, such as cutters and drills for machining, injection molds for manufacturing automobiles, aerospace and aviation and the like.
Drawings
FIG. 1 is an XRD pattern of spray granulated Ti-C agglomerate, tiO 2 -Al-C agglomerate SEM and agglomerate;
FIG. 2 is an XRD pattern of a plasma sprayed TiC coating and TiC-Al 2O3 composite coating;
FIG. 3 is a SEM image of the surface and fracture of a plasma sprayed TiC-Al 2O3 composite coating;
FIG. 4 is a graph of microhardness and fracture toughness of plasma sprayed TiC coatings and TiC-Al 2O3 composite coatings;
FIG. 5 is a graph of friction coefficient and wear rate of a plasma sprayed TiC coating and TiC-Al 2O3 composite coating;
Detailed Description
The invention will be described in further detail below with reference to the embodiments of the accompanying drawings, it being noted that the embodiments described below are intended to facilitate the understanding of the invention and are not meant to be limiting in any way.
In the embodiment, the granularity of Ti powder is 10-48 mu m, the granularity of graphite (or carbon black) is 1-5 mu m, the granularity of Al powder is 5-10 mu m, the granularity of TiO 2 is 10-30 mu m, the granularity of spray granulating Ti-C agglomerated powder is 38-74 mu m, the mass of graphite (or carbon black) is 10-20% of the mass of Ti powder, the granularity of spray granulating TiO 2 -Al-C agglomerated powder is 40-74 mu m, and the ratio among TiO 2, al and C is 3:2:3 or 3:4:3; the two kinds of agglomerated powder with different proportions are mechanically stirred and mixed to be used as spraying composite powder, and the main phases of the coating after plasma spraying deposition are TiC and Al 2O3, and the coating contains a small amount of TiO x and residual Al phase.
Example 1:
In the embodiment, the grain size of Ti powder is 18 mu m, the grain size of graphite powder is 3 mu m, the grain size of Al powder is 5 mu m, the grain size of TiO 2 powder is 10 mu m, two kinds of agglomerated powder are obtained through spray granulation, tiC-Al 2O3 composite coating is prepared by mechanically mixing according to a certain proportion through a plasma spraying process, and the main phases of the coating are TiC and Al 2O3. The fine dispersed Al 2O3 is distributed in the areas of gaps, holes or cracks of the TiC coating lamellar, so that the porosity of the coating is greatly reduced, a compact composite coating is obtained, and meanwhile, the growth of TiC crystal grains is inhibited to obtain the crystal grain fine (submicron or even nano-scale) composite coating.
The preparation method of the coating comprises the following steps:
(1) Putting the deoiled 45# steel matrix sample into a TPS-1 pneumatic sand blaster, and performing sand blasting treatment to obtain a matrix surface with the roughness Ra of 2.5-13.0/mu m; ultrasonic vibration is carried out to remove gravel and drying is carried out, thus obtaining a 45# steel matrix sample with clean and rough surface, and the binding force between the matrix and the coating is increased.
(2) Weighing 200g of titanium powder and 40g of graphite powder by an electronic balance, and performing spray granulation to obtain Ti-C agglomerated powder with the granularity of 38-74 mu m, wherein the mass of the graphite powder is 20% of that of the Ti powder; and similarly, weighing 90g of TiO 2 powder, 90g of Al powder and 60g of graphite powder, spraying and granulating to obtain TiO 2 -Al-C agglomerated powder with the granularity of 40-74 mu m, and mechanically mixing 10g of TiO 2 -Al-C agglomerated powder with 100g of Ti-C agglomerated powder to obtain the spray composite powder.
(3) Before the coating is sprayed, a Ni-Al bonding layer with the thickness of 60-100 mu m is sprayed on the surface of the coarsened 45# steel substrate, wherein the granularity of 90wt.% Ni-Al powder is 40-70 mu m. The Ni-Al bonding layer can relieve thermal stress caused by expansion coefficient difference between the coating and the matrix, and improve bonding strength between the composite coating and the matrix.
(4) The powder feeding device is utilized to send the mechanically mixed spraying composite powder into a plasma flame flow, the self-propagating reaction between Ti and C is ignited based on Gao Wenyan flows, the thermit reaction and carbothermic reaction between TiO 2, al and C are performed, tiC and Al 2O3 products are synthesized in situ and are rapidly and synchronously deposited on the surface of a Ni/Al bonding layer, and the nano TiC-Al 2O3 composite coating with the thickness of 300-450 mu m is obtained after solidification and crystallization, which is specifically expressed as follows: the substrate is fixed on a spraying workbench, the working current 550A, the arc voltage 65V, the powder feeding speed of 3.5L/min, the spraying distance of 100mm, the spraying angle of 90 degrees, the argon flow of 45L/min, the argon pressure of 0.7MPa, the hydrogen flow of 6L/min and the pressure of 0.6MPa are regulated.
FIG. 1 is an XRD pattern of the spray dried Ti-C agglomerate TiO 2 -Al-C agglomerate SEM and agglomerate described above. It can be seen that the agglomerated powder after spray granulation has high sphericity and high fluidity, the granularity meets the plasma spraying requirement, and the agglomerated powder is directly sprayed after mechanical mixing.
FIG. 2 shows XRD patterns of the TiC coating and TiC-Al 2O3 composite coating prepared as described above. As can be seen, the coating prepared by the method has TiC and Al 2O3 as main phases, and contains a small amount of TiO x and residual Al phase.
FIG. 3 is an SEM image of the surface and fracture of the TiC-Al 2O3 composite coating prepared as described above. The graph shows that the coating has a typical lamellar structure, the coating grains after solidification and crystallization are fine (submicron or even nanometer), and fine Al 2O3 is dispersed and distributed at interlayer holes, cracks and gaps, so that the porosity of the coating is greatly reduced, and the compact composite coating is obtained.
And (3) carrying out microhardness and microscopic indentation test experiments on the TiC coating and the TiC-Al 2O3 composite coating, wherein the load is 100g and the load is 15s. Microhardness was obtained by measuring the indentation size and the crack size, and the fracture toughness of the coating was evaluated by using the crack propagation work, and the results are shown in fig. 4. Compared with a single TiC coating, although the microhardness of the composite coating prepared by the method is slightly lower than that of the TiC coating (only 3.4 percent of reduction), the fracture toughness of the composite coating is improved by 29 percent.
And carrying out friction and wear tests on the TiC coating and the TiC-Al 2O3 composite coating. The pin-disc sliding friction mode is adopted, the upper friction pair is a silicon carbide ceramic ball with the diameter of 15mm and the Mohs hardness of 9.2, the lower friction pair is an experimental block with a TiC coating or a TiC-Al 2O3 composite coating, the load is 40N, the friction time is within 30min, and the friction coefficient and the wear rate are shown in figure 5. Compared with a single TiC coating, the abrasion rate of the composite coating prepared by the method is reduced from 6×10 -3mm3 to 2.7×10 -3mm3 under the same friction experiment condition, the friction coefficient is reduced from 0.54 to 0.43, namely the abrasion rate and the friction coefficient are respectively reduced by about 55% and 20%, and the abrasion resistance is obviously improved.
Example 2:
In the embodiment, the granularity of Ti powder is 18 mu m, the granularity of graphite powder is 3 mu m, 200g of titanium powder and 40g of graphite powder are weighed by an electronic balance, and the Ti-C agglomerated powder with the granularity of 38-74 mu m is obtained by spray granulation, wherein the mass of the graphite powder is 20% of the mass of the Ti powder; and similarly weighing 90g of graphite powder with the granularity of 3 mu m, 60g of Al powder with the granularity of 5 mu m and 90g of TiO 2 powder with the granularity of 10 mu m, spraying and granulating to obtain TiO 2 -Al-C agglomerated powder with the granularity of 40-74 mu m, and mechanically stirring and mixing 100g of Ti-C agglomerated powder and 20g of TiO 2 -Al-C agglomerated powder to obtain the spray composite powder. The composite coating with TiC and Al 2O3 as main phases is obtained after plasma spraying deposition
The preparation method of the coating comprises the following steps:
And (3) feeding the spraying composite powder into a plasma flame flow by using a powder feeding device, and spraying the powder to the surface of the bonding layer to obtain the TiC-Al 2O3 composite coating, wherein the mass of the TiO 2 -Al-C agglomerated powder is 10% of that of the Ti-C agglomerated powder, and other steps are the same as those of the example 1.
The XRD pattern of the TiC-Al 2O3 composite coating prepared by the method is similar to that shown in figure 2, the main phases are TiC and Al 2O3, the main phases contain a small amount of TiO x and residual Al phases, and the diffraction peak height of the residual phases is increased.
The SEM image of the surface and fracture of the TiC-Al 2O3 composite coating prepared by the method is similar to that shown in figure 3, the coating still has a typical lamellar structure, and Al 2O3 is dispersed and distributed in the areas of TiC lamellar gaps, holes, cracks and the like, but the porosity of the coating is increased.
The TiC-Al 2O3 composite coating prepared above was subjected to microhardness measurement and microindentation test as in example 1. The microhardness and fracture toughness tested were similar to those of fig. 4, from which it can be seen that the coating microhardness was significantly reduced (16% reduction) and fracture toughness was improved.
The TiC-Al 2O3 composite coating prepared above was subjected to the frictional wear test as in example 1. The coefficient of friction and wear rate of the coating were improved to 0.5 to 0.55 with the coefficient of friction of example 1 (0.4 to 0.45) similar to that of fig. 5.
Example 3:
in this example, ti powder particle size is 48 μm, graphite powder particle size is 5 μm, 200g of titanium powder and 40g of graphite powder are weighed by an electronic balance, ti-C agglomerated powder with particle size of 38-74 μm is obtained by spray granulation, wherein the mass of graphite powder is 10% of that of Ti powder, 90g of graphite powder with particle size of 5 μm, 60g of Al powder with particle size of 10 μm and 90g of TiO 2 powder with particle size of 30 μm are weighed by the same method, tiO 2 -Al-C agglomerated powder with particle size of 40-74 μm is obtained by spray granulation, and then 100g of Ti-C agglomerated powder and 20g of TiO 2 -Al-C agglomerated powder are mechanically stirred and mixed to obtain spray composite powder. The composite coating with TiC and Al 2O3 as main phases is obtained after plasma spraying deposition
The preparation method of the coating comprises the following steps:
And (3) feeding the stirred and mixed spraying composite powder into a plasma flame flow by utilizing a powder feeding device, and spraying the powder to the surface of the bonding layer to obtain the TiC-Al 2O3 composite coating, wherein the mass of TiO 2 -Al-C agglomerated powder in the spraying composite powder accounts for 20% of the mass of the Ti-C agglomerated powder, the granularity of the Ti powder is 48 mu m, the granularity of the graphite powder is 5 mu m, the granularity of the Al powder is 10 mu m, the granularity of the TiO 2 powder is 30 mu m, and other steps are the same as in example 1.
The XRD pattern of the TiC-Al 2O3 composite coating prepared above is similar to that shown in figure 2, and the number and the height of diffraction peaks of the main phases TiC and Al 2O3 are obviously increased.
The SEM image of the surface and fracture of the TiC-Al 2O3 composite coating prepared by the method is similar to that shown in figure 3, the coating still has a typical lamellar structure, al 2O3 is dispersed and distributed in the areas of TiC lamellar gaps, holes, cracks and the like, but the porosity of the coating is greatly increased (more than 15%).
The TiC-Al 2O3 composite coating prepared above was subjected to microhardness and microindentation test as in example 1. The microhardness and fracture toughness of the test are similar to those of FIG. 4, and it can be seen that the hardness of the coating is reduced by more than 24%, and the fracture toughness is improved by 32%.
The TiC-Al 2O3 composite coating prepared above was subjected to the frictional wear test as in example 1. The coefficient of friction and wear rate tested were similar to that of fig. 5, from which it was seen that the coefficient of friction of the coating was slightly reduced, but the wear rate was greatly increased.
The foregoing description of the preferred embodiments of the invention is not intended to limit the invention to the particular embodiments disclosed, but on the contrary, the intention is to cover all modifications, equivalents, and alternatives falling within the spirit and scope of the invention.
The invention is not a matter of the known technology.
Claims (7)
1. A nano TiC-Al 2O3 composite coating and a preparation method thereof are characterized by comprising the following steps:
Step 1, carrying out surface purification and roughening treatment on a sample matrix by adopting a sand blasting method, wherein the matrix material is a metal or nonmetal material, and sand grains are corundum sand or silicon carbide sand;
Step 2, preparing Ti-C agglomerated powder with the granularity of 38-74 mu m by taking Ti powder and graphite (or carbon black) as raw materials through spray granulation, and preparing TiO 2 -Al-C agglomerated powder with the granularity of 40-74 mu m by adopting spray granulation, wherein the granularity of the Ti powder is 10-48 mu m, the granularity of the graphite (or carbon black) is 1-5 mu m, the granularity of the Al powder is 5-10 mu m, and the granularity of TiO 2 is 10-30 mu m;
Step 3, mixing the spray granulation Ti-C agglomerated powder and the TiO 2 -Al-C agglomerated powder by mechanical stirring to form spraying composite powder, wherein the mass of the TiO 2 -Al-C powder is 0-30% of the mass of the Ti-C agglomerated powder;
Step 4, pre-spraying a Ni/Al bonding layer with the thickness of 60-100 mu m on the surface of the sand blasting matrix by adopting a plasma spraying technology;
Step 5, feeding the mechanical mixed composite powder into a high-temperature plasma flame flow by adopting a powder feeding device, igniting self-propagating reaction between Ti and C based on Gao Wenyan flows, carrying out thermit reaction and carbothermic reduction reaction between TiO 2, al and C, synthesizing TiC and Al 2O3 products in situ, rapidly depositing the products on the surface of a Ni/Al bonding layer, and solidifying and crystallizing to obtain the nano TiC-Al 2O3 composite coating with the thickness of 300-450 mu m;
Wherein the spraying parameters are set as follows: the working current is 400-600A, the arc voltage is 50-75V, the argon flow is 20-50L/min, the hydrogen flow is 5-15L/min, the powder feeding rate is 2-5L/min, the spraying distance is 80-120 mm, the argon is used as plasma gas and powder feeding gas, and the hydrogen is used as combustion gas.
2. The nano TiC-Al 2O3 composite coating and its preparation method as claimed in claim 1, wherein the substrate in the step 1 is metal or non-metal material, and the metal material is carbon steel, alloy steel, aluminum alloy, titanium alloy, etc.
3. The nano TiC-Al 2O3 composite coating and the preparation method thereof as claimed in claim 1, wherein the graphite powder used in the step 2 is 10-20% of the Ti powder in mass.
4. The nano TiC-Al 2O3 composite coating and its preparation method as claimed in claim 1, wherein the parameters used for mechanical stirring in the step 3 are as follows: stirring time is 5-15 min, and stirring speed is 20-40 r/min.
5. The nano TiC-Al 2O3 composite coating and the preparation method thereof as claimed in claim 1, wherein the ratio of the three components in the TiO 2 -Al-C agglomerated powder sprayed and granulated in the step 3 is 3:3:2 or 3:3:4.
6. The nano TiC-Al 2O3 composite coating and the preparation method thereof as claimed in claim 1, wherein the Ni-Al bonding layer sprayed in the step 4 is 90wt.% Ni-Al alloy powder, and the granularity is 40-70 μm.
7. The nano TiC-Al 2O3 composite coating and the preparation method thereof as claimed in claim 1, wherein the spraying angle in the step 5 is 90 degrees, the argon pressure is 0.6-0.8 MPa, and the hydrogen pressure is 0.6-0.8 MPa.
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