CN112795919A - Composite coating material for improving friction performance of TC4 alloy and preparation method thereof - Google Patents
Composite coating material for improving friction performance of TC4 alloy and preparation method thereof Download PDFInfo
- Publication number
- CN112795919A CN112795919A CN202110286872.9A CN202110286872A CN112795919A CN 112795919 A CN112795919 A CN 112795919A CN 202110286872 A CN202110286872 A CN 202110286872A CN 112795919 A CN112795919 A CN 112795919A
- Authority
- CN
- China
- Prior art keywords
- composite coating
- coating material
- alloy
- parts
- improving
- 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
- B22F1/142—Thermal or thermo-mechanical treatment
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
Abstract
The invention discloses a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof. The composite coating material is obtained by adopting raw materials through a laser cladding process, and comprises the following raw materials: metallic cobalt, metallic copper and Ti3SiC2. The composite coating utilizes metal cobalt as a toughening phase in a coating system, and the hardness, wear resistance and corrosion resistance of the composite coating are improved; ternary lubricant Ti3SiC2TiC is formed in the cladding process, the TiC is taken as a reinforcing phase, the coating performance is obviously improved, and meanwhile, the TiC is used as a reinforcing phaseCompact TiO is generated in the process of high-temperature friction and abrasion2And SiO2The self-lubricating property of the coating is improved by the oxide film; the soft metal Cu improves the heat conduction, electric conduction, self-lubricating property and tribological property of the composite coating.
Description
Technical Field
The invention belongs to the technical field of composite materials, and particularly relates to a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
Background
The service environment of the aircraft engine is very harsh and is simultaneously affected by high temperature, high pressure, high rotating speed and negative effects caused by gas corrosion, so the requirements on the material are relatively special and strict. The Ti-6Al-4V (TC 4) alloy is one of the common materials for parts such as compressor blades, disks, casings and the like of aeroengines, is widely applied due to the advantages of corrosion resistance, high specific strength, high temperature resistance and the like, but has the defects of low surface hardness, low temperature resistance and the like, so that the service life of the alloy is greatly shortened. Therefore, the development of a composite coating with good tribological properties and improved service life of engine components on the surface of a TC4 alloy substrate is one of the problems to be solved in the industry at present. In order to improve the tribological performance of the TC4 alloy matrix, Ni60-Ti is adopted in the related art3SiC2The alloy powder is subjected to laser cladding to prepare the composite self-lubricating coating on the surface of the TC4 alloy. But have a limited effect on improving the wear resistance of the substrate.
At present, the methods for preparing various composite coatings at home and abroad mainly comprise spraying, electroplating, physical vapor deposition, laser cladding and the like. The bonding strength between the coating prepared by spraying and the substrate is low; electroplating is harmful to the environment; the physical vapor deposition rate is relatively slow. The laser cladding technology is one of the most economical technologies for preparing the self-lubricating coating due to high energy density and good operability, and the substrate and the coating can form good metallurgical bonding and have high bonding strength. In addition, the laser cladding technology can also be used for preparing composite coatings with different mechanical and chemical properties by changing cladding process parameters.
Therefore, it is required to develop a composite coating material for improving the tribological performance of the TC4 alloy, and the self-lubricating property of the material is good.
Disclosure of Invention
The first technical problem to be solved by the invention is as follows: a composite coating material for improving the friction performance of TC4 alloy has high self-lubricating performance.
The second technical problem to be solved by the invention is as follows: a preparation method of the composite coating material.
In order to solve the first technical problem, the technical scheme provided by the invention is as follows: a composite coating material for improving the tribological performance of TC4 alloy is obtained by adopting raw materials through a laser cladding process, and comprises the following raw materials: metallic cobalt, metallic copper and Ti3SiC2。
The cobalt serves as a toughening phase in the coating system and has the characteristics of large amorphous forming capacity, high hardness, good wear resistance, good corrosion resistance and the like; ternary lubricant Ti3SiC2TiC can be formed in the cladding process, is ceramic particles with the advantages of high melting point, high hardness, good thermal stability and the like, can be used as a reinforcing phase to obviously improve the performance of a coating, and can also generate compact TiO in the high-temperature friction and wear process2And SiO2The self-lubricating property of the coating is improved by the oxide film; the soft metal Cu has excellent heat conducting, electric conducting and self-lubricating performances and better tribological performance.
Ternary lubricant Ti3SiC2Due to the excellent properties of the ceramic and the metal, the alloy has good self-lubricating property and wear resistance at high temperature, and the soft metal Cu has excellent thermal conductivity and is beneficial to effective dissipation of frictional heat, so that the temperature of a contact area is reduced.
According to some embodiments of the invention, the composite coating material comprises the following raw materials in parts by weight: 74-86 parts of metal cobalt and Ti3SiC24 to 6 parts and 10 to 20 parts of metallic copper.
According to some embodiments of the invention, the composite coating material comprises the following raw materials in parts by weight: 85 parts of metallic cobalt and Ti3SiC25 parts and 10 parts of metallic copper.
According to some embodiments of the invention, the composite coating material has a thickness of 1mm or more.
According to some embodiments of the invention, the metallic cobalt has a purity of 99.99% or greater.
According to some embodiments of the invention, the metallic cobalt has a particle size of 50 μm to 150 μm.
The composite coating material for improving the tribological performance of the TC4 alloy has at least the following beneficial effects: the composite coating utilizes metal cobalt as a toughening phase in a coating system, and the hardness, wear resistance and corrosion resistance of the composite coating are improved; ternary lubricant Ti3SiC2TiC is formed in the cladding process, the TiC is used as a reinforcing phase, the coating performance is obviously improved, and compact TiO is generated in the high-temperature friction and wear process2And SiO2The self-lubricating property of the coating is improved by the oxide film; the soft metal Cu improves the heat conduction, electric conduction, self-lubricating property and tribological property of the composite coating, and compared with the metal such as chromium adopted in the related technology, the environmental pollution is reduced.
To solve the second technical problem, the present invention provides the following technical solutions: the preparation method of the composite coating material comprises the following steps:
mixing the raw materials, and covering the powder on the surface of the treated TC4 alloy substrate by using a synchronous powder feeding method; and carrying out laser irradiation cladding treatment for multiple times to obtain the composite coating material.
According to some embodiments of the invention, the laser irradiation cladding process comprises the following process parameters: the output power of the laser is 1.5 kW-1.7 kW, the diameter of a light spot is 2 mm-2.5 mm, the scanning speed is 6 mm/s-13 mm/s, the powder feeding speed is 12 g/min-14 g/min, the defocusing amount is-1 mm or 1mm, the overlapping rate is 50%, and the energy density is 45J/mm2~75 J/mm2。
According to some embodiments of the invention, the laser irradiation cladding process comprises the following process parameters: the output power of the laser is 1.6 kW, the diameter of a light spot is 2mm, the scanning speed is 13mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 61.5J/mm2。
The calculation formula of the energy density is as follows:
wherein K is the energy density (kJ/mm)2) P is the laser output power (kW), D is the spot diameter (mm), and V is the scanning speed (mm/s).
According to some embodiments of the invention, the means of mixing the raw materials comprises the following operations: ball-milling the raw materials to obtain a mixture, and drying the mixture;
wherein the ball milling time is 2-2.5 h.
According to some embodiments of the invention, the temperature of the drying is 80 ℃ to 120 ℃.
According to some embodiments of the invention, the drying time is 2h to 2.5 h.
According to some embodiments of the invention, the laser has a wavelength of 800nm to 1000 nm.
According to some embodiments of the invention, the treated TC4 alloy substrate is a lapped TC4 alloy substrate.
According to some embodiments of the invention, the sanding process uses at least one of 400 mesh, 600 mesh, 800 mesh, 1200 mesh, and 2000 mesh sandpaper.
The preparation method of the composite coating material provided by the embodiment of the invention has at least the following beneficial effects: the invention adopts laser cladding technology and adopts Co-Ti3SiC2Preparing a composite coating on the surface of a TC4 alloy base material by using-Cu alloy powder as a raw material, wherein Co is a toughening phase, and Ti is3SiC2The Cu is a lubricating phase and is a reinforcing phase, and the Cu, the Cu and the lubricating phase have good synergistic effect on improvement of the friction performance of the composite coating. Compared with the TC4 alloy base material, the average hardness of the composite coating is improved by 2.07-2.39 times, and the surface wear resistance of the TC4 alloy base material is greatly improved.
Drawings
The invention is further described with reference to the following figures and examples, in which:
FIG. 1 is an SEM image of metallic cobalt used in example one of the present invention and comparative example one;
FIG. 2 shows Ti used in example one and comparative example one of the present invention3SiC2SEM picture of (1);
FIG. 3 is an SEM image of a mixture used in example one of the present invention and comparative example one;
FIG. 4 is a scanning electron micrograph of a cross section of a composite coating obtained according to an embodiment of the present invention;
FIG. 5 is a scanning electron micrograph of a cross section of a composite coating obtained in example two of the present invention;
FIG. 6 shows XRD patterns of the composite coatings obtained in the first to second embodiments of the present invention and the first embodiment of the present invention;
FIG. 7 is a microhardness distribution diagram of a cross section of a composite coating obtained in the first to second examples of the present invention and the first comparative example;
FIG. 8 is a graph showing the coefficient of friction at 25 ℃ of the composite coating obtained in examples one to two of the present invention and comparative example one and the TC4 alloy substrate of comparative example two;
FIG. 9 shows the friction coefficients at 300 ℃ of the composite coatings obtained in examples one to two of the present invention and comparative example one and the TC4 alloy substrate of comparative example two;
FIG. 10 is a graph showing the friction coefficients at 600 ℃ of the composite coatings obtained in examples one to two of the present invention and comparative example one and the TC4 alloy substrate of comparative example two;
FIG. 11 is a graph comparing the average coefficient of friction of composite coatings obtained in examples one-two of the present invention and comparative example one with that of a TC4 alloy substrate in comparative example two;
FIG. 12 is a graph showing a comparison of wear rates at different temperatures for composite coatings obtained in examples one-two of the present invention and comparative example one and a TC4 alloy substrate of comparative example two;
FIG. 13 is an SEM image of the wear surface and swarf at room temperature for the composite coatings obtained in examples one-two of the present invention and comparative example one and the TC4 alloy substrate of comparative example two;
FIG. 14 is an SEM image of the abraded surface and abrasive dust at 300 ℃ for the composite coating obtained in examples one to two of the present invention and comparative example one and the TC4 alloy substrate of comparative example two;
FIG. 15 is an SEM image of the abraded surface and abrasive dust at 600 ℃ for the composite coating obtained in examples one-two of the present invention and comparative example one and the TC4 alloy substrate of comparative example two;
reference numerals:
n1, comparative example one; n2, embodiment one; n3, example two; TC4, comparative example two; RT, room temperature (25 ℃).
Detailed Description
The concept and technical effects of the present invention will be clearly and completely described below in conjunction with the embodiments to fully understand the objects, features and effects of the present invention. It is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments, and those skilled in the art can obtain other embodiments without inventive effort based on the embodiments of the present invention, and all embodiments are within the protection scope of the present invention.
The first embodiment of the invention is as follows: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The composite coating material is composed of the following raw materials in parts by weight: 5wt.% Ti3SiC210wt.% Cu and the balance Co.
The preparation method of the composite coating material comprises the following steps:
s1, putting the raw materials into a DECO-PBM-V-0.4L vertical planetary ball mill for ball milling for 2 hours to obtain an alloy powder mixture, and drying for 2 hours in a vacuum drying oven at 100 ℃;
s2, sequentially using sand paper of 400 meshes, 600 meshes, 800 meshes, 1200 meshes and 2000 meshes to polish the TC4 alloy base material;
s3, scanning the surface of the TC4 alloy base material by adopting an LDM-8060 powder feeding type laser through a synchronous powder feeding method, and forming a composite coating material on the surface of the TC4 alloy base material; wherein the output power is 1.6 kW, the diameter of a light spot is 2mm, the scanning speed is 13mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 61.5J/mm2. The calculation formula of the energy density is shown as follows:
wherein K is the energy density (kJ/mm)2) P is the laser output power (kW), D is the spot diameter (mm), and V is the scanning speed (mm/s).
The second embodiment of the invention is as follows: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
the composite coating material is composed of the following raw materials in parts by weight: 20wt.% Cu, 5wt.% Ti3SiC2And the balance being Co.
The third embodiment of the invention is as follows: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
step S3: scanning the surface of the TC4 alloy base material by adopting an LDM-8060 powder feeding type laser in a synchronous powder feeding method to form a composite coating material on the surface of the TC4 alloy base material; wherein the output power is 1.6 kW, the diameter of a light spot is 2mm, the scanning speed is 13mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 61.5J/mm2。
The fourth embodiment of the invention is as follows: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
step S3: scanning the surface of the TC4 alloy base material by adopting an LDM-8060 powder feeding type laser in a synchronous powder feeding method to form a composite coating material on the surface of the TC4 alloy base material; wherein the output power is 1.6 kW, the diameter of a light spot is 2.5mm, the scanning speed is 13mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 49.23J/mm2。
The fifth embodiment of the invention is as follows: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
step S3: adopts LDM-8060 powder feeding type laser to synchronously feed powder at TC4Scanning the surface of the gold base material to form a composite coating material on the surface of the TC4 alloy base material; wherein the output power is 1.6 kW, the diameter of a light spot is 2mm, the scanning speed is 13mm/s, the powder feeding speed is 12g/min, the defocusing amount is 1mm, the lap joint rate is 50%, and the energy density is 61.54J/mm2。
The first comparative example of the present invention is: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
the composite coating material is composed of the following raw materials in parts by weight: 5wt.% Ti3SiC2And the balance being Co.
The second comparative example of the present invention is: a substrate of the commercially available TC4 alloy.
The third comparative example of the present invention is: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
s3, scanning the surface of the TC4 alloy base material by adopting an LDM-8060 powder feeding type laser through a synchronous powder feeding method, and forming a composite coating material on the surface of the TC4 alloy base material; wherein the output power is 0.8 kW, the diameter of a light spot is 2mm, the scanning speed is 6mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 66.67J/mm2。
Comparative example four of the present invention is: a composite coating material for improving the tribological performance of TC4 alloy and a preparation method thereof.
The difference from the first embodiment is as follows:
step S3: scanning the surface of the TC4 alloy base material by adopting an LDM-8060 powder feeding type laser in a synchronous powder feeding method to form a composite coating material on the surface of the TC4 alloy base material; wherein the output power is 1.2 kW, the diameter of a light spot is 2mm, the scanning speed is 10 mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 60J/mm2。
Test example:
taking the performance test of the example I as an example, and comparing the wear resistance with the wear resistance of the comparative example I and the comparative example II, the performance of the composite coating material of the invention is illustrated; the apparent morphology of the inventive and comparative examples was tested using SEM.
The morphology of the metal cobalt selected in the embodiment of the invention and the first comparative example is shown in fig. 1, and it can be known from fig. 1 that the morphology of the metal cobalt is spherical.
Ti used in examples of the present invention and comparative examples3SiC2The morphology of Ti is shown in FIG. 2, and can be seen from FIG. 23SiC2The shape of the powder is blocky powder.
The morphology of the mixture powder obtained in the inventive example and comparative example I is shown in FIG. 3, and it can be seen from FIG. 3 that metallic cobalt and Ti are present after ball milling3SiC2The appearance has no obvious change.
The cross-sectional shapes of the composite coatings prepared in the embodiment of the invention and the comparative example are approximately similar, so that the cross-sectional shapes of the composite coatings prepared in the embodiment one and the embodiment two are selected for specific analysis, the cross-sectional SEM of the composite coating prepared in the embodiment one is shown in figure 4, and the thickness of the coating is about 1.05 mm from figure 4; example two composite coatings were obtained by cross-sectional SEM imaging of fig. 5, which shows that the coating thickness was about 1.45 mm, and that a composite coating with good metallurgical bonding was formed on the TC4 alloy substrate, but a small amount of microcracks and undissolved Co were observed in the bonding region, and the interface of the melting zone was wavy, indicating that the temperature was not uniform, resulting in insufficient melting of some Co.
XRD patterns of composite coating materials prepared in comparative example one (N1), example one (N2) and example two (N3) of the present invention are shown in FIG. 6, phases of composite coatings prepared in example one (N2) and example two (N3) are substantially the same, and gamma-Co, CoC and the like are identifiedxAnd a strong diffraction peak of Cu, wherein a metastable metal gamma-Co solid solution having an fcc structure is a protruding phase and can exist stably at 417 ℃ or higher, and C strongly affects the stress anisotropy of Co, so that the Co group of the cemented carbide is also a carbide CoCxThe alloy has higher hardness, and can improve the hardness and the wear resistance of a cladding layer. With the simultaneous presence of Ti3SiC2、Ti5Si4And weak diffraction peak of TiC, indicating Ti added3SiC2The particles partially decompose during laser irradiation to form TiC and Ti5Si4. In addition to the above phases, the diffraction peaks of Cu were clearly detected in examples one (N2) and two (N3), which indicates that copper hardly reacts during laser cladding, and the intensity of the diffraction peak of Cu is relatively weak because the Cu content of example one (N2) is less than that of example two (N3). In addition, the gamma-Co diffraction peak in comparative example one (N1) was stronger than that in examples one (N2) and two (N3) because the Co content in comparative example one (N1) was relatively higher. In addition, no oxides were found because the experiments were performed in an argon atmosphere.
The average microhardness of the composite coatings prepared in the first and second examples of the invention is shown in FIG. 7, and it can be seen from FIG. 7 that the average microhardness of the composite coatings N1 (first comparative example), N2 (first example) and N3 (second example) is 907.47 HV0.5、786.66 HV0.5And 865.97 HV0.5About TC4 alloy matrix (380 HV)0.5) 2.07 to 2.39 times of the total amount of the active ingredient. The reasons for the increased hardness are attributed to the following four reasons: firstly, dispersion strengthening: the hard phase in the composite coating is uniformly distributed in the cladding layer under the action of strong convection generated in the molten pool; secondly, solid solution strengthening: the condensation speed of the molten pool is high, so that part of alloy elements are not fully reacted and finally dissolved in solid solution; thirdly, fine crystal strengthening: the large supercooling degree inhibits the growth of crystal grains to cause fine grain strengthening; fourthly, the composite alloy powder system has excellent performance and can improve the mechanical property of the composite coating.
In order to test the high-temperature tribological properties of the composite coatings prepared in the first to second embodiments of the present invention and the first comparative example, the present invention performed an experiment using a HT-1000 high-temperature friction and wear tester, with test parameters as shown in table 1 and test results as shown in table 2.
TABLE 1 high-temperature frictional wear test parameters of composite coatings prepared in the first to second inventive examples and the first comparative example
TABLE 2 average friction factor of TC4 alloy for composite coatings of inventive examples one-two and comparative example one and comparative example two
The friction factors of the composite coatings prepared in the first to second embodiments of the invention and the first to second comparative examples at different temperatures are shown in FIGS. 8 to 10, the average friction factor test results are shown in tables 2 and 11, and the Co-Ti-based coating prepared by the invention can be obtained by combining the tables 2 and 8 to 113SiC2The Cu alloy powder can improve the friction reduction performance of the TC4 alloy matrix, and the composite coatings of the example I and the example II show extremely excellent friction reduction performance at room temperature (25 ℃), but are poorer than the coating of the comparative example I at high temperature.
Measuring the wear profile and the volume of a sample by using an M-500 probe type material surface wear scar measuring instrument, and calculating the wear rate by using a formula as follows:
wherein W is the wear rate (mm)3N · m), F is the load (N), d is the sliding distance (m), V is the wear volume (mm)3)。
The test data are shown in table 3, and the alignment of the test results is shown in fig. 12.
TABLE 3 wear Rate (. times.10) of TC4 alloy for the composite coatings of inventive examples one to two and comparative example one and comparative example two-5mm3/N·m）
The data in table 3 and fig. 12 show that the wear rate of the composite coatings prepared in the first and second examples is low at room temperature, and the wear resistance of the matrix is improved.
At room temperature, the wear and abrasion appearance of the TC4 alloy matrix, the composite coatings prepared in the first embodiment and the second embodiment and the composite coating prepared in the first comparative embodiment are shown in FIG. 13; in the figure, (a) TC4 alloy wear surfaces, (b) TC4 alloy wear debris, (c) N1 wear surfaces, (d) N1 wear debris, (e) N2 wear surfaces, (f) N2 wear debris, (g) N3 wear surfaces, (h) N3 wear debris. It is known from the figure that the TC4 alloy matrix surface has a large amount of furrows, severe plastic deformation and abrasive wear, and abrasive dust is granular. The wear marks on the surfaces of the three composite coatings are obviously lighter than those of the matrix, and the three composite coatings show good wear resistance, wherein furrows and plastic deformation of the coating of the comparative example are obviously reduced, a plurality of irregular pits appear on the surfaces, and the abrasive dust is irregular blocks and particles and has larger size than the matrix. The coating surfaces of the first and second examples were more flat than the first comparative example, and had partial peeling pits, and the amount of swarf was significantly reduced.
At 300 ℃, the wear and abrasive dust shapes of the TC4 alloy matrix, the composite coatings prepared in the first embodiment and the second embodiment and the composite coating prepared in the first comparative embodiment are shown in FIG. 14; in the figure, (a) TC4 alloy wear surfaces, (b) TC4 alloy wear debris, (c) N1 wear surfaces, (d) N1 wear debris, (e) N2 wear surfaces, (f) N2 wear debris, (g) N3 wear surfaces, (h) N3 wear debris. The stripping pits and chips on the surface of the TC4 alloy matrix are known from the figure, which shows that the matrix has three action mechanisms of plastic deformation, adhesive abrasion and abrasive wear. Comparative example one surface had abrasive wear and slight adhesive wear. In the first embodiment, a "glaze layer" appears on the surface, because in the abrasion process, the lubricating phase is obviously diffused to the contact surface of the coating and the ceramic ball, the friction heating and the pressure act on the lubricating phase to form a compact glaze layer, the ceramic ball can abrade the glaze layer after repeatedly sliding, and simultaneously, a new protective glaze layer is formed on the abrasion trace. Thus, the glaze layer undergoes a cyclic process of formation, loss and reformation during the dry slip process. The glaze layer phenomenon of the second coating is lighter than that of the first coating, a small amount of pits are formed, and the abrasive dust is agglomerated.
At 600 ℃, the wear and abrasive dust shapes of the TC4 alloy matrix, the composite coatings prepared in the first embodiment and the second embodiment and the composite coating prepared in the first comparative embodiment are shown in FIG. 15; in the figure, (a) TC4 alloy wear surfaces, (b) TC4 alloy wear debris, (c) N1 wear surfaces, (d) N1 wear debris, (e) N2 wear surfaces, (f) N2 wear debris, (g) N3 wear surfaces, (h) N3 wear debris. It can be seen from the figure that the wear surface of the TC4 alloy substrate was rough with severe furrowing, scratching parallel to the sliding direction, delamination and plastic deformation, the coating surface of comparative example one had slight adhesive wear, the plastic deformation was significantly reduced, the size of the swarf was finer than that of the substrate, the surface of example one had peeling pits, the surface of example two had slight adhesive wear, and the swarf agglomerated, but the surface wear of examples one and two was significantly less than that of the substrate and comparative example one.
The substrate and the coating of the third comparative example do not form good metallurgical bonding and cause uneven distribution of surface materials, the composite coating prepared by the fourth comparative example has obvious defects such as air holes and the like on the surface, the composite coating prepared by the first example is obviously superior to the composite coating prepared by the third comparative example and the fourth comparative example, the macroscopic quality of the surface is good, the cross section diagram in the application shows that the substrate and the coating form good metallurgical bonding, no macroscopic cracks, air holes and other defects are found, and the dilution rate is low.
In conclusion, the invention adopts the laser cladding technology and adopts Co-Ti3SiC2Preparing a composite coating on the surface of a TC4 alloy base material by using-Cu alloy powder as a raw material, wherein Co is a toughening phase, and Ti is3SiC2The Cu is a lubricating phase and is a reinforcing phase, and the Cu, the Cu and the lubricating phase have good synergistic effect on improvement of the friction performance of the composite coating. Compared with the TC4 alloy base material, the average hardness of the composite coating is improved by 2.07-2.39 times, and the surface wear resistance of the TC4 alloy base material is greatly improved.
The embodiments of the present invention have been described in detail with reference to the accompanying drawings, but the present invention is not limited to the above embodiments, and various changes can be made within the knowledge of those skilled in the art without departing from the gist of the present invention. Furthermore, the embodiments of the present invention and the features of the embodiments may be combined with each other without conflict.
Claims (10)
1. A composite coating material for improving the tribological performance of TC4 alloy is characterized byThe method comprises the following steps: is prepared from raw materials by a laser cladding process; the composite coating material comprises the following raw materials in parts by weight: 74-86 parts of metal cobalt and Ti3SiC24 to 6 parts and 10 to 20 parts of metallic copper.
2. The composite coating material for improving the tribological performance of the TC4 alloy according to claim 1, wherein: the composite coating material comprises the following raw materials in parts by weight: 85 parts of metallic cobalt and Ti3SiC25 parts and 10 parts of metallic copper.
3. The composite coating material for improving the tribological performance of the TC4 alloy according to claim 1, wherein: the thickness of the composite coating material is more than 1 mm.
4. The composite coating material for improving the tribological performance of the TC4 alloy according to claim 1 or 2, wherein: the purity of the metal cobalt is more than 99.99 percent.
5. The composite coating material for improving the tribological performance of the TC4 alloy according to claim 1 or 2, wherein: the particle size of the metal cobalt is 50-150 mu m.
6. A process for preparing a composite coating material according to any one of claims 1 to 5, characterized in that: the method comprises the following steps:
mixing the raw materials, and covering the powder on the surface of the treated TC4 alloy substrate by using a synchronous powder feeding method; and carrying out laser irradiation cladding treatment to obtain the composite coating material.
7. The method of claim 6, wherein: the technological parameters of the laser irradiation cladding treatment comprise: the output power of the laser is 1.5 kW-1.7 kW, the diameter of a light spot is 2 mm-2.5 mm, the scanning speed is 6 mm/s-13 mm/s, the powder feeding speed is 12 g/min-14 g/min, the defocusing amount is-1 mm or 1mm, the overlapping rate is 50%, and the energy density is 45J/mm2~75 J/mm2(ii) a Preferably, the laser irradiation cladding treatment process parameters are as follows: the output power of the laser is 1.6 kW, the diameter of a light spot is 2mm, the scanning speed is 13mm/s, the powder feeding rate is 12g/min, the defocusing amount is-1 mm, the lap joint rate is 50 percent, and the energy density is 61.5J/mm2。
8. The method of claim 6, wherein: the raw material mixing mode comprises the following operations: ball-milling the raw materials to obtain a mixture, and drying the mixture;
wherein the ball milling time is 2-2.5 h.
9. The method of claim 8, wherein: the drying temperature is 80-120 ℃; the drying time is 2-2.5 h.
10. The method of claim 6, wherein: the wavelength of the laser is 800 nm-1000 nm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110286872.9A CN112795919B (en) | 2021-03-17 | 2021-03-17 | Composite coating material for improving friction performance of TC4 alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110286872.9A CN112795919B (en) | 2021-03-17 | 2021-03-17 | Composite coating material for improving friction performance of TC4 alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112795919A true CN112795919A (en) | 2021-05-14 |
| CN112795919B CN112795919B (en) | 2021-07-20 |
Family
ID=75817161
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110286872.9A Active CN112795919B (en) | 2021-03-17 | 2021-03-17 | Composite coating material for improving friction performance of TC4 alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112795919B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115433934A (en) * | 2022-08-03 | 2022-12-06 | 中南林业科技大学 | Alloy powder for laser cladding, coating, preparation method and application thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011524466A (en) * | 2008-06-06 | 2011-09-01 | ダウ グローバル テクノロジーズ エルエルシー | Metal-infiltrated silicon titanium and aluminum carbide bodies |
| CN104018155A (en) * | 2014-06-06 | 2014-09-03 | 江苏大学 | Method for preparing Ti-Si-C coating on surface of titanium metal |
| JP2015175041A (en) * | 2014-03-17 | 2015-10-05 | 国立大学法人東北大学 | Production method of amorphous soft magnetic alloy powder |
| CN106191747A (en) * | 2016-08-13 | 2016-12-07 | 安徽鼎恒再制造产业技术研究院有限公司 | A kind of Co Cu Mn TiO2nano coating and preparation method thereof |
| CN106834866A (en) * | 2016-12-28 | 2017-06-13 | 江西理工大学 | Application of the titanium silicon-carbon in hard alloy |
| CN108707894A (en) * | 2018-06-09 | 2018-10-26 | 沈阳工业大学 | Powder and process used in a kind of laser melting coating self-lubricating abrasion-resistant cobalt-base alloys |
-
2021
- 2021-03-17 CN CN202110286872.9A patent/CN112795919B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011524466A (en) * | 2008-06-06 | 2011-09-01 | ダウ グローバル テクノロジーズ エルエルシー | Metal-infiltrated silicon titanium and aluminum carbide bodies |
| US8863816B2 (en) * | 2008-06-06 | 2014-10-21 | Dow Global Technologies Llc | Metal-infiltrated titanium—silicon-carbide and titanium—aluminum-carbide bodies |
| JP2015175041A (en) * | 2014-03-17 | 2015-10-05 | 国立大学法人東北大学 | Production method of amorphous soft magnetic alloy powder |
| CN104018155A (en) * | 2014-06-06 | 2014-09-03 | 江苏大学 | Method for preparing Ti-Si-C coating on surface of titanium metal |
| CN106191747A (en) * | 2016-08-13 | 2016-12-07 | 安徽鼎恒再制造产业技术研究院有限公司 | A kind of Co Cu Mn TiO2nano coating and preparation method thereof |
| CN106834866A (en) * | 2016-12-28 | 2017-06-13 | 江西理工大学 | Application of the titanium silicon-carbon in hard alloy |
| CN108707894A (en) * | 2018-06-09 | 2018-10-26 | 沈阳工业大学 | Powder and process used in a kind of laser melting coating self-lubricating abrasion-resistant cobalt-base alloys |
Non-Patent Citations (3)
| Title |
|---|
| DEXUAN YANG等: "Highly conductive wear resistant Cu/Ti3SiC2(TiC/SiC) co-continuous", 《JOURNAL OF ADVANCED CERAMICS 》 * |
| 刘其斌等: "《激光制备先进材料及其应用》", 31 May 2016, 冶金工业出版社 * |
| 张宝昌等: "《有色金属及其热处理》", 31 October 1993, 西北工业大学出版社 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115433934A (en) * | 2022-08-03 | 2022-12-06 | 中南林业科技大学 | Alloy powder for laser cladding, coating, preparation method and application thereof |
| CN115433934B (en) * | 2022-08-03 | 2023-12-05 | 中南林业科技大学 | Alloy powder and coating for laser cladding, and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112795919B (en) | 2021-07-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR100751742B1 (en) | Spray powder, thermal spraying process using it, and sprayed coating | |
| CN113122840A (en) | Tough wear-resistant strengthening layer and preparation method thereof | |
| CN109252158A (en) | A kind of tantalum carbide gradient composite coating and preparation method thereof | |
| CN112795919B (en) | Composite coating material for improving friction performance of TC4 alloy and preparation method thereof | |
| CN111979451A (en) | Composite coating material, stainless steel surface composite coating and preparation method thereof | |
| CN113106443B (en) | 304 stainless steel coated with self-lubricating wear-resistant composite coating and preparation method thereof | |
| CN110894603B (en) | Material for preparing wear-resistant self-lubricating coating, wear-resistant self-lubricating coating and preparation method | |
| CN114951696A (en) | Method for manufacturing FeCrTiV on surface of ferrite/martensite steel by laser additive manufacturing 0.5 Ni 0.5 High entropy alloy coatings and methods | |
| CN1644319A (en) | Manufacture of single-layer diamond grinder | |
| Miyamoto et al. | Fabrication of new cemented carbide containing diamond coated with nanometer‐sized SiC particles | |
| JP2000234136A (en) | Cemented carbide, coated cemented carbide and production thereof | |
| CN115351279B (en) | Coated cemented carbide cutting tool | |
| CN114686883B (en) | Cutting tool with gradient multilayer coating and preparation method thereof | |
| JP2011177799A (en) | Diamond-coated cutting tool | |
| JP2011200987A (en) | Diamond-coated cutting tool | |
| JPS5928628B2 (en) | Surface coated cemented carbide tools | |
| CN111250695A (en) | Iron-based binding agent carborundum grinding wheel special for railway steel rail grinding and preparation method thereof | |
| CN106623902A (en) | Titanium-containing honing oilstone and preparation method and application thereof | |
| CN115611636B (en) | Surface modified cubic boron nitride powder and preparation method and application thereof | |
| CN117070821B (en) | WC-Co metal ceramic particle gradient reinforced copper-based wear-resistant coating and preparation method thereof | |
| CN115044856B (en) | Preparation method of abrasion self-repairing sealing coating | |
| CN115449787B (en) | Nickel-based/W/C alloy coating and preparation method thereof | |
| CN117802494A (en) | Preparation method of metal surface particle reinforced metal-based wear-resistant corrosion-resistant coating | |
| JP2002173774A (en) | Cvd coating of titanium-boron and chromium-boron for diamond | |
| Liu et al. | Effect of TiO2 films on diamond: oxidation resistance and wear performance |
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 |