CN115287647A - Laser cladding ceramic particle reinforced aluminum-based cladding layer and preparation method thereof - Google Patents
Laser cladding ceramic particle reinforced aluminum-based cladding layer and preparation method thereof Download PDFInfo
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- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 158
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 154
- 239000002245 particle Substances 0.000 title claims abstract description 99
- 238000005253 cladding Methods 0.000 title claims abstract description 93
- 238000004372 laser cladding Methods 0.000 title claims abstract description 58
- 239000000919 ceramic Substances 0.000 title claims abstract description 37
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 239000000843 powder Substances 0.000 claims abstract description 150
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 84
- 239000002131 composite material Substances 0.000 claims abstract description 82
- 238000000498 ball milling Methods 0.000 claims abstract description 40
- 238000000034 method Methods 0.000 claims abstract description 36
- 239000011261 inert gas Substances 0.000 claims abstract description 24
- 238000005516 engineering process Methods 0.000 claims abstract description 21
- 238000005238 degreasing Methods 0.000 claims abstract description 20
- 239000000463 material Substances 0.000 claims abstract description 17
- 238000002156 mixing Methods 0.000 claims abstract description 15
- 238000009833 condensation Methods 0.000 claims abstract description 12
- 230000005494 condensation Effects 0.000 claims abstract description 12
- 238000001704 evaporation Methods 0.000 claims abstract description 12
- 230000008020 evaporation Effects 0.000 claims abstract description 12
- 239000000956 alloy Substances 0.000 claims description 48
- 229910045601 alloy Inorganic materials 0.000 claims description 36
- 238000012216 screening Methods 0.000 claims description 19
- YXFVVABEGXRONW-UHFFFAOYSA-N Toluene Chemical compound CC1=CC=CC=C1 YXFVVABEGXRONW-UHFFFAOYSA-N 0.000 claims description 16
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- 230000008018 melting Effects 0.000 claims description 16
- 238000002844 melting Methods 0.000 claims description 16
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 10
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- 229910052729 chemical element Inorganic materials 0.000 claims description 8
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- 239000002994 raw material Substances 0.000 claims description 7
- 238000001291 vacuum drying Methods 0.000 claims description 7
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- 239000012159 carrier gas Substances 0.000 claims description 5
- 239000003054 catalyst Substances 0.000 claims description 5
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- 239000000203 mixture Substances 0.000 claims description 3
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- 238000013329 compounding Methods 0.000 claims 2
- 238000001125 extrusion Methods 0.000 claims 1
- 239000000758 substrate Substances 0.000 abstract description 28
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 15
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- 229910018520 Al—Si Inorganic materials 0.000 abstract description 8
- 238000013461 design Methods 0.000 abstract description 2
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- 239000002184 metal Substances 0.000 abstract description 2
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- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 8
- 239000013078 crystal Substances 0.000 description 7
- 230000010287 polarization Effects 0.000 description 7
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- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- 238000004140 cleaning Methods 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 239000011858 nanopowder Substances 0.000 description 5
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- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
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- 230000007613 environmental effect Effects 0.000 description 1
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- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 238000002161 passivation Methods 0.000 description 1
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- 238000005728 strengthening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- 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
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- 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
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
-
- 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
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- 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
- B22F1/145—Chemical treatment, e.g. passivation or decarburisation
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y40/00—Manufacture or treatment of nanostructures
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/06—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron
- C01B21/072—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron with aluminium
- C01B21/0722—Preparation by direct nitridation of aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention belongs to the technical field of aluminum alloy laser cladding, and particularly relates to a laser cladding ceramic particle reinforced aluminum-based cladding layer, and further discloses a preparation method thereof. The invention relates to a preparation method of a laser cladding ceramic particle reinforced aluminum-based cladding layer, which aims at the design of preparing a nano TiN particle reinforced aluminum-based high-corrosion-resistance cladding layer by laser cladding, and is characterized in that nano TiN ceramic particles are added into aluminum-based powder, aluminum-based powder is prepared by adopting a vacuum ball milling technology, nano TiN ceramic particles are prepared by adopting an inert gas evaporation and condensation method, tiN/aluminum-based composite powder is prepared by mixing a material mixing technology and a degreasing technology in Metal Injection Molding (MIM), and then a high-density Al-Si composite cladding layer is prepared on a 6061 substrate by adopting a laser cladding mode.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy laser cladding, and particularly relates to a laser cladding ceramic particle reinforced aluminum-based cladding layer, and further discloses a preparation method thereof.
Background
The aluminum alloy material has become a common material in the industrial fields of aerospace, automobiles, electric power, ships and the like due to the characteristics of small density, high specific strength, good corrosion resistance and the like. However, the aluminum alloy material is easy to generate thermal deformation in the manufacturing process due to the defects of low hardness, no wear resistance, large heat conduction coefficient, poor thermal stability, active chemical property, easy oxidation and blackening in a humid environment and the like, and the moisture and oxide crystal water adsorbed in the aluminum alloy oxide film are easy to decompose hydrogen in the manufacturing process to form air holes, so that the density of a formed part is reduced. Therefore, it is common knowledge in the art to improve the hardness and wear resistance of the aluminum alloy matrix by surface modification techniques to improve the application properties.
The laser cladding technology is a surface modification technology which takes high-energy laser as an energy source, rapidly melts and solidifies a powder material and a thin layer on the surface of a substrate, and then forms a cladding layer with high bonding strength (metallurgical bonding) with the substrate. The method has the characteristics of high bonding strength, uniform structure, high utilization rate, high efficiency, environmental friendliness, economy, quickness and the like, and becomes an important method for the aluminum alloy surface modification technology. The Particle reinforced Aluminum alloy composite material is named PAMCs (particulate reinforced Aluminum Matrix Composites), is an Aluminum-based composite material with hard particles as a reinforcing phase, has high specific stiffness, high specific strength, high hardness and excellent wear resistance, and can not only keep good compatibility and wettability of original powder and a Matrix, but also play a remarkable reinforcing effect on a cladding layer.
For example, chinese patent CN114381727A discloses a laser cladding forming method for the surface of an aluminum alloy plate, which uses a powder-wire composite cladding technical scheme and assists side injection of B4C particles into an Al-based cladding layer, thereby effectively improving the wear resistance of the laser cladding layer. Also, as disclosed in chinese patent CN108796498A, the method for producing a ceramic phase by a laser cladding aluminum alloy surface self-reaction is applied in the scheme, which uses a method in which mixed powder reacts with aluminum element in a molten aluminum alloy matrix to produce a ceramic phase, thereby improving the bonding strength between the cladding layer and the aluminum alloy matrix, and further improving the wear resistance and corrosion resistance of the aluminum alloy surface.
In the studied PAMCs, tiN particles are expected to be used as a composite material reinforcing phase to obviously improve the comprehensive performance of a matrix due to higher wear resistance, thermal stability, electrical conductivity and chemical stability. However, in the conventional method for preparing composite powder based on ball milling mixing in the laser cladding technology, the phenomenon of uneven distribution of TiN particles is easy to occur, and further the original powder cannot be well coated, so that the method becomes a problem to be solved urgently for preparing an aluminum alloy cladding layer with excellent comprehensive performance.
Disclosure of Invention
Therefore, the technical problem to be solved by the invention is to provide a preparation method of a laser cladding ceramic particle reinforced aluminum-based cladding layer, which is characterized in that nano TiN particle reinforced aluminum-based composite powder is used for processing the composite cladding layer so as to improve the phenomenon that the original powder cannot be well clad due to uneven distribution of the nano powder during ball milling of the composite powder;
the second technical problem to be solved by the invention is to provide the nano TiN particle reinforced aluminum-based high corrosion-resistant cladding layer prepared by the method.
In order to solve the technical problem, the preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer comprises the following steps:
(1) Selecting alloy raw materials according to the elements and the proportion of the selected aluminum-based alloy powder, mixing, and carrying out vacuum melting treatment;
(2) Performing ball milling treatment on the treated material, and performing particle size screening on the obtained aluminum-based alloy powder for later use;
(3) Under the protection of inert gas, preparing TiN nano-particles by using an inert gas evaporation condensation method;
(4) Mixing the aluminum-based alloy powder obtained in the step (2) and the TiN nano particles obtained in the step (3), degreasing and screening the mixture to obtain TiN/aluminum-based composite powder for later use;
(5) And preparing a cladding layer on the surface of the matrix from the aluminum-based composite powder by adopting a laser cladding technology.
Specifically, in the step (1), the chemical element ratio of the aluminum-based alloy powder includes: si:9.5-9.9wt%, mg:0.2-0.3wt%, fe:0.1-0.2wt%, and the balance of Al;
preferably, the temperature of the vacuum melting treatment step is 700-800 ℃, and the heat preservation time is 1-2h.
Specifically, in the step (2);
the parameters of the ball milling treatment step comprise: a vacuum planetary ball milling method is adopted, the ball milling speed is controlled to be 400-550r/min, the ball milling is stopped for 10 minutes within 30-50 minutes, and the ball milling time is 4-6 hours;
in the screening step, the particle size range of the aluminum-based alloy powder is controlled to be 50-120 mu m, and the D50 is controlled to be 70-80 mu m.
Specifically, in the step (3), the control parameters of the inert gas evaporation condensation method include: the inert gas pressure is 5000-6000Pa, the arc striking current is 150-200A, the voltage is 25-30V, and the arc striking time is 1-3 hours.
Specifically, in the step (4), the mixing treatment step includes a step of extruding and mixing the aluminum-based alloy powder, the TiN nanoparticles and a binder under the protection of inert gas;
preferably, the mass ratio of the aluminum-based alloy powder, the TiN nanoparticles and the binder is 48.5:1.5:50;
preferably, the binder comprises a poly-toluene.
Specifically, in the step (4), the degreasing step control parameters include: nitrogen is used as protective gas and carrier gas, nitric acid gas is used as a degreasing catalyst, the introduction amount is 1g/min, the temperature in the furnace is 130 ℃, and the degreasing time is 2 hours.
Specifically, in the step (4), in the sieving step, the particle size range of the composite powder is controlled to be 50-120 μm, and the D50 is controlled to be 60-70 μm.
Specifically, in the step (5), the control parameters of the laser cladding technology include: the laser power is 4000-5000W, the scanning speed is 6-10mm/s, the powder feeding speed is 5g/min, the spot diameter is 4mm, and the lapping rate is 80%.
Specifically, the step (5) further comprises the step of drying the TiN/aluminum-based composite powder in a vacuum drying oven at the temperature of 80 ℃ and the vacuum degree of-0.06 MPa.
The invention also discloses the laser cladding ceramic particle reinforced aluminum-based cladding layer prepared by the method.
The invention relates to a preparation method of a laser cladding ceramic particle reinforced aluminum-based cladding layer, which aims at the design of preparing a nano TiN particle reinforced aluminum-based high-corrosion-resistance cladding layer by laser cladding, and comprises the steps of adding nano TiN ceramic particles into aluminum-based powder, preparing the aluminum-based powder by adopting a vacuum ball milling technology, preparing nano TiN ceramic particles by adopting an inert gas evaporation and condensation method, preparing TiN/aluminum-based composite powder by mixing a material mixing technology and a degreasing technology in Metal Injection Molding (MIM), and preparing a high-density Al-Si composite cladding layer on a 6061 substrate by adopting a laser cladding mode. According to the invention, the nano TiN ceramic particles are added into the aluminum-based powder, the powder material is prepared by mixing in the MIM and degreasing technology, not only is the sphericity high, but also the nano TiN particles are uniformly dispersed and distributed on the surfaces of the aluminum-based powder particles, the TiN/aluminum-based composite powder element is close to a 6061 matrix, and the melting point interval is close to each other, so that the TiN/aluminum-based composite cladding layer has better phase fusibility with the 6061 matrix, the TiN particles are uniformly distributed in the cladding layer under the convection action, the corrosion resistance of the Al-Si cladding layer is improved, the phenomenon that the original powder cannot be well clad due to uneven distribution of the nano powder during ball-milling composite powder is effectively improved, and the powder material has wide application prospects in the aspects of surface strengthening and repairing of aluminum alloy components.
The preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer provided by the invention has the advantages that through reasonable component proportion and comprehensive powder preparation technology, the prepared nano TiN particle reinforced aluminum-based high-corrosion-resistance cladding layer has smooth surface and high sphericity, is uniformly dispersed and distributed on the surface of the aluminum-based particle, has good forming applicability with the aluminum-based cladding layer, and is finally prepared.
According to the preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer, by designing a reasonable component ratio and matching with the characteristic of rapid melting by laser cladding, tiN nano particles are uniformly distributed around a crystal boundary in the cladding layer, so that the growth of crystal grains is inhibited, the structure of the composite cladding layer is more refined, the segregation of eutectic Si in the cladding layer is reduced, the density of the cladding layer is improved, a passivation film generated by the cladding layer is more compact, and the corrosion resistance of the cladding layer is improved. Meanwhile, the TiN particles have excellent corrosion resistance, are uniformly distributed around the crystal boundary, and a small amount of TiN particles are distributed in the crystal grains, so that the electrolyte diffusion is hindered, corrosion channels and paths are reduced, and the corrosion resistance of the composite cladding layer is comprehensively improved.
In the laser cladding ceramic particle reinforced aluminum-based cladding layer, the nano TiN particle reinforced aluminum-based composite powder is optimally proportioned and comprises the following chemical elements in percentage by mass: 9.85%, mg:0.28%, fe:0.17%, tiN:3% and the balance of Al. Wherein the content of the first and second substances,
si element can improve the fluidity of the aluminum-based cladding layer, and the manufacturing performance and the wear resistance are better when the Si content in the alloy is higher;
TiN is ceramic particles with stable chemical properties, excellent hardness, corrosion resistance, abrasion resistance and oxidation resistance, and has a melting point higher than that of aluminum-based alloy, so that the growth of crystal grains is inhibited, and the crystal grains are refined; however, the content of TiN particles cannot be too high, and the high content of TiN particles can cause the linear expansion coefficient of the cladding layer alloy to be increased, particularly the hot cracking tendency to be larger, and cause the cladding layer to have serious crack defects;
the aluminum-based alloy powder and the 6061 matrix belong to Al-Si alloy, and the aluminum-based alloy powder and the 6061 matrix have good phase fusibility, good alloy airtightness, small density, high thermal conductivity, low thermal expansion coefficient, good manufacturability, mechanical property, corrosion resistance, excellent welding performance and the like.
In the laser cladding ceramic particle reinforced aluminum-based cladding layer, the nano TiN particle reinforced aluminum-based composite powder is optimally proportioned, the particle size distribution of the nano TiN particle reinforced aluminum-based composite powder is similar to that of aluminum-based powder, the element distribution is uniform, the nano TiN particle reinforced aluminum-based composite powder has better laser absorptivity than the aluminum-based powder, and the melting points and the melting temperature ranges of the nano TiN particle reinforced aluminum-based composite powder and the aluminum-based powder are similar to each other, so that the nano TiN particle reinforced aluminum-based composite powder has good forming applicability when the nano TiN particle reinforced aluminum-based composite powder and the aluminum-based powder are formed by laser cladding.
Drawings
In order that the present disclosure may be more readily and clearly understood, the following detailed description of the present disclosure is provided in connection with specific embodiments thereof and the accompanying drawings, in which,
FIG. 1 is an element distribution, EDX analysis and SEM micrograph of TiN/aluminum-based composite powder prepared in example 1 of the present invention; wherein, (a) is the element distribution of the TiN/aluminum-based composite powder, (b) is EDX analysis, and (c) is an SEM micrograph of the TiN/aluminum-based composite powder;
FIG. 2 is a partial SEM micrograph of a TiN/Al-based composite cladding layer prepared according to example 1 of the present invention; wherein, (a) an upper portion, (b) a middle portion, (c) a bottom portion, (d) a high power micrograph;
FIG. 3 is an element distribution, EDX analysis and SEM micrograph of an aluminum-based powder prepared in comparative example 1 of the present invention; wherein, (a) is the element distribution of the aluminum-based powder, (b) is EDX analysis, and (c) is an SEM micrograph of the aluminum-based powder;
FIG. 4 is a partial SEM micrograph of an aluminum-based cladding layer prepared according to comparative example 1 of the present invention; wherein (a) an upper portion, (b) a middle portion, (c) a bottom portion;
FIG. 5 is a dynamic polarization curve of a 6061 substrate with an aluminum-based cladding layer prepared in comparative example 2 and a TiN/aluminum-based composite cladding layer prepared in example 2, respectively;
FIG. 6 is a metallographic micrograph of three sets of comparative aluminum-based cladding layers in comparative example 2.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the embodiments of the present invention.
Example 1
The preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer comprises the following steps:
(1) Preparing aluminum-based powder, wherein the chemical elements according to the mass fraction are Si:9.85%, mg:0.28%, fe:0.17 percent of Al and the balance of Al are weighed; after the raw materials are fully mixed, carrying out vacuum melting treatment under the conditions that the temperature is 750 ℃ and the heat preservation time is 2 hours to obtain an alloy material;
(2) Ball-milling the obtained alloy material by adopting a vacuum planetary ball mill, controlling the ball-milling rotating speed to be 500r/min, ball-milling for 40 minutes, stopping the ball-milling machine for 10 minutes, and ball-milling for 6 hours; obtaining aluminum-based powder, and performing particle size screening to control the alloy powder within a certain particle size range; the particle size range of the aluminum-based composite powder after screening is controlled to be 50-120 mu m, and the D50 is controlled to be 70.16 mu m;
(3) Preparing nano TiN powder particles with the purity of 99.5% by an inert gas evaporation condensation method under the protection of inert gas (Ar) for later use; the specific parameters of the TiN nano powder particles prepared by the inert gas evaporation condensation method are as follows: the inert gas pressure is 6000Pa, the arcing current is 200A, the voltage is 28V, and the arcing time is 2 hours;
(4) Placing the aluminum-based composite powder screened in the step (2) and the TiN nano particles in an MIM mixer, taking poly-toluene as a binder in an argon protective environment, adding the TiN and aluminum-based alloy powder into the binder (poly-toluene) in batches according to a certain proportion, wherein the mass ratio of the TiN to the aluminum-based alloy powder to the binder is 3;
(5) Degreasing and screening the mixed composite powder material to ensure that the screened composite alloy powder is in a certain particle size range; specifically, nitrogen is used as a protective gas and a carrier gas, nitric acid gas is used as a degreasing catalyst, the introduction amount is 1g/min, the temperature in the furnace is 130 ℃, and the degreasing time is 2 hours; the particle size range of the screened composite powder is 50-120 mu m, and the D50 is 68.64 mu m; the obtained TiN/aluminum-based composite powder can be subjected to vacuum packaging for later use;
the element distribution, EDX analysis and SEM micrograph of the TiN/aluminum-based composite powder obtained in the example are shown in the attached figure 2, wherein, (a) is the element distribution of the TiN/aluminum-based composite powder, (b) is the EDX analysis, and (c) is the SEM micrograph of the TiN/aluminum-based composite powder;
(6) Putting the prepared TiN/aluminum-based composite powder in a vacuum drying box with the temperature of 80 ℃ and the vacuum degree of-0.06 MPa, drying for 4 hours, putting the powder into a high-precision double-path adjustable powder feeder, and preparing to prepare a cladding layer on a 6061 aluminum substrate; meanwhile, a 6061 aluminum alloy substrate is used for carrying out surface treatment on the experiment, an oxide layer and burrs on the surface of the substrate material are removed by polishing with abrasive paper, impurities on the surface of the substrate material are removed by cleaning with an ethanol solution, and the experiment is carried out immediately after drying;
(7) Preparing a high-density Al-Si composite cladding layer on the surface of a 6061 matrix by adopting a coaxial powder feeding type laser cladding technology; the parameters for controlling laser cladding are as follows: the laser power is 4400W, the scanning speed is 8mm/s, the powder feeding speed is 5g/min, the spot diameter is 4mm, and the lap joint rate is 80%.
The local SEM micrograph of the TiN/aluminum-based composite cladding layer prepared by the embodiment is shown in a figure 2; wherein, (a) the upper part, (b) the middle part, (c) the bottom part, and (d) the high power micrograph.
In this example, the dynamic polarization curve of the 6061 substrate and the TiN/aluminum-based composite cladding layer is shown in fig. 6. The TiN/Al-based composite cladding layer prepared in this example, E, was tested corr ＝-508.7mV，I corr ＝0.098μA/cm 2 . Polarization potential E of the cladding layer prepared in this example corr Higher, polarization current density I corr And the corrosion resistance of the TiN/aluminum-based composite cladding layer prepared by the method is excellent.
Example 2
The preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer comprises the following steps:
(1) Preparing aluminum-based powder, wherein the chemical elements according to the mass fraction are Si:9.5%, mg:0.3%, fe:0.1 percent of Al and the balance of Al are weighed; fully mixing the raw materials, and carrying out vacuum melting treatment under the conditions that the temperature is 700 ℃ and the heat preservation time is 2 hours to obtain an alloy material;
(2) Ball-milling the obtained alloy material by adopting a vacuum planetary ball mill, controlling the ball-milling rotating speed to be 400r/min, carrying out ball-milling for 50 minutes, stopping the ball-milling machine for 10 minutes, and carrying out ball-milling for 5 hours; obtaining aluminum-based powder, screening the aluminum-based powder by particle size, and controlling the alloy powder within a certain particle size range; the particle size range of the aluminum-based composite powder after screening is controlled to be 50-120 mu m, and the D50 is controlled to be 71.22 mu m;
(3) Preparing nano TiN powder particles with the purity of 99.5% by an inert gas evaporation condensation method under the protection of inert gas (Ar) for later use; the specific parameters of the TiN nano powder particles prepared by the inert gas evaporation condensation method are as follows: the pressure of inert gas is 5000Pa, the arcing current is 150A, the voltage is 25V, and the arcing time is 2 hours;
(4) Putting the aluminum-based composite powder screened in the step (2) and the TiN nano particles into an MIM mixer, adding the TiN and the aluminum-based alloy powder into a binder (poly-toluene) in batches according to a certain proportion by taking poly-toluene as the binder in an argon protective environment, wherein the mass ratio of the TiN to the aluminum-based alloy powder to the binder is 3;
(5) Degreasing and screening the mixed composite powder material to ensure that the screened composite alloy powder is in a certain particle size range; specifically, nitrogen is used as a protective gas and a carrier gas, nitric acid gas is used as a degreasing catalyst, the introduction amount is 1g/min, the temperature in the furnace is 130 ℃, and the degreasing time is 2 hours; the particle size range of the screened composite powder is 50-120 mu m, and the D50 is 67.83 mu m; the obtained TiN/aluminum-based composite powder can be subjected to vacuum packaging for later use;
(6) Putting the prepared TiN/aluminum-based composite powder in a vacuum drying oven with the temperature of 80 ℃ and the vacuum degree of-0.06 MPa, drying for 4 hours, putting the powder into a high-precision double-path adjustable powder feeder, and preparing a cladding layer on a 6061 aluminum substrate; meanwhile, a 6061 aluminum alloy substrate is used for carrying out surface treatment on the experiment, an oxide layer and burrs on the surface of the substrate material are removed by polishing with abrasive paper, impurities on the surface of the substrate material are removed by cleaning with an ethanol solution, and the experiment is carried out immediately after drying;
(7) Preparing a high-density Al-Si composite cladding layer on the surface of a 6061 matrix by adopting a coaxial powder feeding type laser cladding technology; the parameters for controlling laser cladding are as follows: the laser power is 4400W, the scanning speed is 8mm/s, the powder feeding speed is 5g/min, the spot diameter is 4mm, and the lap joint rate is 80%.
Example 3
The preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer comprises the following steps:
(1) Preparing aluminum-based powder, wherein chemical elements according to mass fraction are Si:9.9%, mg:0.2%, fe:0.2 percent of Al and the balance of Al are weighed; fully mixing the raw materials, and carrying out vacuum melting treatment under the conditions that the temperature is 800 ℃ and the heat preservation time is 1h to obtain an alloy material;
(2) Ball-milling the obtained alloy material by adopting a vacuum planetary ball mill, controlling the ball-milling rotating speed to be 550r/min, carrying out ball-milling for 30 minutes, stopping the ball-milling machine for 10 minutes, and carrying out ball-milling for 4 hours; obtaining aluminum-based powder, and performing particle size screening to control the alloy powder within a certain particle size range; the particle size range of the aluminum-based composite powder after screening is controlled to be 50-120 mu m, and the D50 is controlled to be 72.64 mu m;
(3) Preparing nano TiN powder particles with the purity of 99.5% by adopting an inert gas evaporation condensation method under the protection of inert gas (Ar) for later use; the specific parameters of the TiN nano powder particles prepared by the inert gas evaporation condensation method are as follows: the pressure of inert gas is 5500Pa, the arc starting current is 180A, the voltage is 30V, and the arc starting time is 2 hours;
(4) Putting the aluminum-based composite powder screened in the step (2) and the TiN nano particles into an MIM mixer, adding the TiN and the aluminum-based alloy powder into a binder (poly-toluene) in batches according to a certain proportion by taking poly-toluene as the binder in an argon protective environment, wherein the mass ratio of the TiN to the aluminum-based alloy powder to the binder is 3;
(5) Degreasing and screening the mixed composite powder material to ensure that the screened composite alloy powder is in a certain particle size range; specifically, nitrogen is used as a protective gas and a carrier gas, nitric acid gas is used as a degreasing catalyst, the introduction amount is 1g/min, the temperature in the furnace is 130 ℃, and the degreasing time is 2 hours; the particle size range of the screened composite powder is 50-120 mu m, and the D50 is 66.53 mu m; the obtained TiN/aluminum-based composite powder can be subjected to vacuum packaging for later use;
(6) Putting the prepared TiN/aluminum-based composite powder in a vacuum drying box with the temperature of 80 ℃ and the vacuum degree of-0.06 MPa, drying for 4 hours, putting the powder into a high-precision double-path adjustable powder feeder, and preparing to prepare a cladding layer on a 6061 aluminum substrate; meanwhile, a 6061 aluminum alloy substrate is used for carrying out surface treatment on the experiment, an oxide layer and burrs on the surface of the substrate material are removed by polishing with abrasive paper, impurities on the surface of the substrate material are removed by cleaning with an ethanol solution, and the experiment is carried out immediately after drying;
(7) Preparing a high-density Al-Si composite cladding layer on the surface of a 6061 matrix by adopting a coaxial powder feeding type laser cladding technology; the parameters for controlling laser cladding are as follows: the laser power is 4400W, the scanning speed is 8mm/s, the powder feeding speed is 5g/min, the spot diameter is 4mm, and the lap joint rate is 80%.
Comparative example 1
The preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer comprises the following steps:
(1) Preparing aluminum-based powder, wherein the chemical elements according to the mass fraction are Si:9.85%, mg:0.28%, fe:0.17 percent of Al and the balance of Al are weighed; after the raw materials are fully mixed, carrying out vacuum melting treatment under the conditions that the temperature is 750 ℃ and the heat preservation time is 2 hours to obtain an alloy material;
(2) Ball-milling the obtained alloy material by adopting a vacuum planetary ball mill, wherein the ball-milling rotating speed is 450r/min, the ball-milling is stopped for 10 minutes after 40 minutes, and the ball-milling time is 6 hours; obtaining aluminum-based powder, and performing particle size screening to control the alloy powder within a certain particle size range; the particle size range of the aluminum-based composite powder after screening is controlled to be 50-120 mu m, the D50 is controlled to be 70.78 mu m, and the aluminum-based composite powder can be subjected to vacuum packaging for later use;
the comparative example preparation of an aluminum-based powder element distribution, EDX analysis and SEM micrograph is shown in figure 2; wherein, (a) is the element distribution of the aluminum-based powder, (b) is EDX analysis, and (c) is an SEM micrograph of the aluminum-based powder;
(3) Placing the prepared aluminum-based composite powder in a vacuum drying box with the temperature of 80 ℃ and the vacuum degree of-0.06 MPa, drying for 4 hours, putting the dried powder into a high-precision double-path adjustable powder feeder, and preparing to prepare a cladding layer on a 6061 aluminum substrate; meanwhile, a 6061 aluminum alloy substrate is used for surface treatment in the experiment, an oxide layer and burrs on the surface of the substrate are removed by polishing with sand paper, impurities on the surface of the substrate are removed by cleaning with an ethanol solution, and the experiment is immediately carried out after drying;
(4) Preparing a high-density Al-Si cladding layer on the surface of a 6061 matrix by adopting a coaxial powder feeding type laser cladding technology; the parameters for controlling laser cladding are as follows: the laser power is 4400W, the scanning speed is 8mm/s, the powder feeding speed is 5g/min, the spot diameter is 4mm, and the lap joint rate is 80%.
The local SEM micrograph of the aluminum-based cladding layer prepared by the comparative example is shown in figure 3; wherein, (a) an upper portion, (b) a middle portion, and (c) a bottom portion.
In this comparative example, the dynamic polarization curve of the 6061 substrate and the prepared aluminum-based cladding layer is shown in FIG. 6. Through the test, the aluminum-based cladding layer prepared by the comparative example, E corr ＝-763.9mV，I corr ＝0.166μA/cm 2 . The polarization potential Ecorr of the cladding layer prepared by the comparative example is obviously lower than that of the cladding layer prepared by the example 1, and the polarization current density Icorr is obviously higher than that of the cladding layer prepared by the example 1, which shows that the corrosion resistance of the aluminum-based cladding layer prepared by the comparative example is obviously inferior to that of the TiN/aluminum-based composite cladding layer prepared by the application.
Comparative example 2
The preparation method of the laser cladding ceramic particle reinforced aluminum-based cladding layer comprises the following steps:
(1) Preparing aluminum-based powder, wherein chemical elements according to mass fraction are Si:9.85%, mg:0.28%, fe:0.17 percent of Al and the balance of Al are weighed; fully mixing the raw materials, and carrying out vacuum melting treatment under the conditions that the temperature is 800 ℃ and the heat preservation time is 2 hours to obtain an alloy material;
(2) Ball-milling the obtained alloy material by adopting a vacuum planetary ball mill, wherein the ball-milling rotating speed is 500r/min, the ball-milling is stopped for 10 minutes after 40 minutes, and the ball-milling time is 5 hours; obtaining aluminum-based powder, screening the aluminum-based powder by particle size, and controlling the alloy powder within a certain particle size range; the particle size range of the aluminum-based composite powder after screening is controlled to be 50-120 mu m, the D50 is controlled to be 70.93 mu m, and the aluminum-based composite powder can be subjected to vacuum packaging for later use;
(3) Placing the prepared aluminum-based composite powder in a vacuum drying box with the temperature of 80 ℃ and the vacuum degree of-0.06 MPa, drying for 4 hours, putting the dried powder into a high-precision double-path adjustable powder feeder, and preparing to prepare a cladding layer on a 6061 aluminum substrate; meanwhile, a 6061 aluminum alloy substrate is used for surface treatment in the experiment, an oxide layer and burrs on the surface of the substrate are removed by polishing with sand paper, impurities on the surface of the substrate are removed by cleaning with an ethanol solution, and the experiment is immediately carried out after drying;
(4) Preparing a high-density Al-Si cladding layer on the surface of a 6061 substrate by adopting a coaxial powder feeding type laser cladding technology; controlling parameters of 5g/min of powder feeding speed, 4mm of spot diameter and 80% of lap joint rate of laser cladding, respectively adjusting laser power and scanning speed, controlling parameters of (a) 4000W of laser power and 6mm/s of scanning speed, (b) 4400W of laser power and 8mm/s of scanning speed, and (c) 5000W of laser power and 10mm/s of scanning speed, carrying out three times of comparative laser cladding experiments, and representing proper parameters of laser power and scanning speed according to a metallographic microscopic image of a formed cladding layer.
The nano TiN particle reinforced aluminum-based composite powder is optimized and proportioned, the particle size distribution of the nano TiN particle reinforced aluminum-based composite powder is similar to that of aluminum-based powder, the element distribution is uniform, the nano TiN particle reinforced aluminum-based composite powder has better laser absorption rate characteristic than that of the aluminum-based powder, and the nano TiN particle reinforced aluminum-based composite powder and the aluminum-based powder have similar melting points and melting temperature intervals, so that the nano TiN particle reinforced aluminum-based composite powder and the aluminum-based powder have good forming applicability when being formed by laser cladding. Therefore, the aluminum-based composite powder can be used for preparing two cladding layers by selecting proper process parameters.
The metallographic micrographs of the three groups of laser cladding ceramic particle reinforced aluminum-based cladding layers prepared in the comparative example are shown in the attached figure 6. Wherein, (a) is a metallurgical microscopic picture of the cladding layer prepared by the parameters that the laser power is 4000W and the scanning speed is 6 mm/s; (b) Is a metallurgical microscopic picture of the cladding layer prepared by the parameters that the laser power is 4400W and the scanning speed is 8 mm/s; (c) The method is a metallurgical microscopic picture of the cladding layer prepared by the parameters that the laser power is 5000W and the scanning speed is 10 mm/s.
In the comparative example, the obvious cracks and air holes appear in the cladding layers of the experimental example 1 and the experimental example 3, and the obvious air holes and cracks do not appear in the laser cladding layer of the experimental example 2, which indicates that the laser power and the scanning speed parameters are proper, so that the TiN/aluminum-based composite cladding layer with higher density can be prepared under the process parameters of the laser power of 4400W, the scanning speed of 8mm/s, the powder feeding speed of 5g/min, the spot diameter of 4mm and the lap joint rate of 80%.
The above embodiments of the present invention are described in detail, and the principle and the implementation of the present invention are explained by applying specific embodiments, and the description of the above embodiments is only used to help understanding the method of the present invention and the core idea thereof; meanwhile, for a person skilled in the art, according to the idea of the present invention, there may be variations in the specific embodiments and the application scope, and in summary, the content of the present specification should not be construed as a limitation to the present invention.
Claims (10)
1. A preparation method of a laser cladding ceramic particle reinforced aluminum-based cladding layer is characterized by comprising the following steps:
(1) Selecting alloy raw materials according to the elements and the proportion of the selected aluminum-based alloy powder, mixing, and carrying out vacuum melting treatment;
(2) Performing ball milling treatment on the treated material, and performing particle size screening on the obtained aluminum-based alloy powder for later use;
(3) Preparing TiN nano-particles by using an inert gas evaporation condensation method under the protection of inert gas;
(4) Mixing the aluminum-based alloy powder obtained in the step (2) and the TiN nano particles obtained in the step (3), degreasing and screening the mixture to obtain TiN/aluminum-based composite powder for later use;
(5) And preparing a cladding layer on the surface of the matrix by adopting a laser cladding technology.
2. The method for preparing the laser cladding ceramic particle reinforced aluminum-based cladding layer according to claim 1, wherein in the step (1), the chemical element mixture ratio of the aluminum-based alloy powder comprises: si:9.5-9.9wt%, mg:0.2-0.3wt%, fe:0.1-0.2wt%, and the balance of Al;
preferably, the temperature of the vacuum melting treatment step is 700-800 ℃, and the heat preservation time is 1-2h.
3. The method for preparing a laser cladding ceramic particle reinforced aluminum-based cladding layer according to claim 1 or 2, wherein in the step (2);
the parameters of the ball milling treatment step comprise: a vacuum planetary ball milling method is adopted, the ball milling speed is controlled to be 400-550r/min, the ball milling is stopped for 10 minutes within 30-50 minutes, and the ball milling time is 4-6 hours;
in the screening step, the particle size range of the aluminum-based alloy powder is controlled to be 50-120 mu m, and the D50 is controlled to be 70-80 mu m.
4. The method for preparing a laser cladding ceramic particle reinforced aluminum-based cladding layer according to any one of claims 1 to 3, wherein in the step (3), the control parameters of the inert gas evaporation condensation method comprise: the pressure of inert gas is 5000-6000Pa, the arc starting current is 150-200A, the voltage is 25-30V, and the arc starting time is 1-3 hours.
5. The method for preparing a laser cladding ceramic particle reinforced aluminum-based cladding layer according to any one of claims 1 to 4, wherein in the step (4), the compounding treatment step comprises a step of extrusion compounding the aluminum-based alloy powder, the TiN nano particles and a binder under an inert gas shield;
preferably, the mass ratio of the aluminum-based alloy powder, the TiN nanoparticles and the binder is 48.5:1.5:50;
preferably, the binder comprises a poly-toluene.
6. The method for preparing a laser cladding ceramic particle reinforced aluminum-based cladding layer according to any one of claims 1 to 5, wherein in the step (4), the parameters for controlling the degreasing step comprise: nitrogen is used as protective gas and carrier gas, nitric acid gas is used as a degreasing catalyst, the introduction amount is 1g/min, the temperature in the furnace is 130 ℃, and the degreasing time is 2 hours.
7. The method for preparing a laser cladding ceramic particle reinforced aluminum-based cladding layer according to any one of claims 1 to 6, wherein in the step (4), the particle size of the composite powder is controlled to be in the range of 50 to 120 μm and the D50 is controlled to be in the range of 60 to 70 μm in the sieving step.
8. The method for preparing a laser cladding ceramic particle reinforced aluminum-based cladding layer according to any one of claims 1 to 7, wherein in the step (5), the control parameters of the laser cladding technology comprise: the laser power is 4000-5000W, the scanning speed is 6-10mm/s, the powder feeding speed is 5g/min, the spot diameter is 4mm, and the lap joint rate is 80%.
9. The method for preparing a laser cladding ceramic particle-reinforced aluminum-based cladding layer according to any one of claims 1 to 8, further comprising the step of drying the TiN/aluminum-based composite powder in a vacuum drying oven at 80 ℃ and a vacuum degree of-0.06 MPa in the step (5).
10. A laser clad ceramic particle reinforced aluminum based cladding layer prepared by the method of any one of claims 1 to 9.
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