CN111088485A - Magnesium-based composite material based on gradient cladding and preparation method thereof - Google Patents

Magnesium-based composite material based on gradient cladding and preparation method thereof Download PDF

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CN111088485A
CN111088485A CN201911333231.3A CN201911333231A CN111088485A CN 111088485 A CN111088485 A CN 111088485A CN 201911333231 A CN201911333231 A CN 201911333231A CN 111088485 A CN111088485 A CN 111088485A
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powder
magnesium
cladding
composite material
gradient
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张英乔
靳坤
李志勇
魏守征
郭杰
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North University of China
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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
    • C23C24/106—Coating with metal alloys or metal elements only
    • 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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Abstract

The invention discloses a magnesium-based composite material based on gradient cladding and a preparation method thereof. The coating formed by gradient cladding is compact and has no crack, the layers are in good metallurgical bonding, the hardness, the wear resistance and the corrosion resistance of the coating are greatly improved compared with those of a matrix, and the application range of the magnesium alloy in corrosive and wear environments is expanded.

Description

Magnesium-based composite material based on gradient cladding and preparation method thereof
Technical Field
The invention relates to a magnesium-based composite material and a preparation method thereof, in particular to a magnesium-based composite material based on gradient cladding and a preparation method thereof, and belongs to the field of composite material preparation.
Background
The magnesium alloy has the characteristics of small density, high specific strength and specific stiffness, repeated recycling and the like, is widely applied to the fields of automobiles, aerospace and the like, has low hardness, poor wear resistance and corrosion resistance, is easy to fail prematurely when working in high-temperature, high-speed, heavy-load, wear-resistant and corrosive environments, and limits the application range of the magnesium alloy. By means of the surface modification technology, the surface performance of the magnesium alloy is improved on the premise of keeping the original performance of the material, so that the magnesium alloy can adapt to severe working environment, the application field of the magnesium alloy can be further widened, and the magnesium alloy has certain economic value and application prospect.
The magnesium alloy surface modification technology comprises anodic oxidation, micro-arc oxidation, chemical conversion, electroplating, vapor deposition, plasma spraying and the like, but the problems of thin surface modification layer, high porosity, poor density, untight combination with a matrix, high cost, environmental friendliness and the like generally exist. The laser cladding technology has the advantages of high energy density, high heating and cooling speed, small heat affected zone, high density of the prepared coating, and firm combination with the matrix, and is an ideal magnesium alloy surface modification technology.
The magnesium alloy has low melting point and boiling point, and is seriously evaporated in the high-power laser cladding process, so that the energy input of a laser is usually limited in practical use, but the energy input is reduced, so that the thickness of a coating cannot be increased, powder with a high melting point is difficult to melt, and the finally prepared coating is thin and has poor surface forming even cannot be formed. If a gradient cladding method can be adopted, a layer of coating material with small difference of thermal physical properties such as melting point, boiling point and the like with the magnesium alloy is clad firstly; and a layer of high-melting-point anticorrosive wear-resistant coating material is cladded on the coating, so that the problem can be better solved. On one hand, the coating thickness can be increased by multilayer cladding, and premature exposure of the magnesium alloy under the working condition of surface abrasion and in corrosive media is avoided; on the other hand, high power can be adopted during upper cladding, so that the problems of serious evaporation and high dilution rate caused by direct cladding on the surface of the magnesium alloy are avoided.
Disclosure of Invention
The invention aims to provide a magnesium-based composite material based on gradient cladding and a preparation method thereof, and particularly relates to a magnesium-based composite material prepared by sequentially cladding Al and Al-Ti-Ni/C powder materials on a magnesium alloy matrix.
The invention provides a magnesium-based composite material based on gradient cladding and a preparation method thereof, wherein the magnesium-based composite material takes magnesium alloy as a matrix, adopts Nd: the YAG laser is sequentially coated with a middle transition layer and an upper protective layer on the surface. The invention adopts a pre-coating method, firstly, the powder is mixed into paste by using an adhesive, and the paste is coated on a matrix Mg, and then laser irradiation cladding is carried out. The invention adopts Nd: the YAG laser carries out gradient cladding on the surface of the magnesium alloy, firstly cladding Al powder to prepare a transition layer, and continuously cladding Al-Ti-Ni/C mixed powder to prepare a protective layer, thereby forming a gradient coating with good metallurgical bonding and excellent performance and meeting the use requirements of the gradient coating under the conditions of abrasion and corrosion.
The thermophysical properties of aluminum and magnesium are similar, for example, the melting point of Al is 660 ℃, which is only slightly higher than that of magnesium (649 ℃), the wettability of the aluminum and the magnesium is good, and simultaneously, the hardness of the aluminum is higher than that of the magnesium, and the aluminum has good corrosion resistance. When the surface of the magnesium alloy is subjected to laser cladding, Al is used as a transition layer, and Al powder and the surface of a small amount of magnesium matrix can be simultaneously melted by using small laser energy, so that firm metallurgical connection is formed after cooling and solidification, the evaporation of the magnesium matrix is reduced, and the defects of interface peeling, crack, air hole and the like are prevented. Therefore, the aluminum powder is selected as the transition layer material for magnesium alloy gradient cladding.
The upper protective layer of the invention adopts high-performance mixed metal powder as cladding material. Due to the existence of the Al transition layer, the laser does not directly act on the surface of the magnesium substrate, the problems of magnesium evaporation and high dilution rate do not exist, and larger laser energy can be selected, so that the selectable powder system has a wider range. Binary metal powder, ternary metal powder, metal and ceramic mixed powder and the like can be used, but the selected cladding powder material and an Al intermediate transition layer material have good thermophysical compatibility and wettability so as to ensure that the intermediate transition layer and a protective layer are well combined. The invention uses Al, Ti and Ni/C (nickel-coated carbon) mixed powder as upper protective layer laser cladding powder. The content of Al powder is more so as to ensure good interface bonding between the intermediate layer and the protective layer and gradient transition of performance; addition of Ti and Ni/C powder can form Al with Al3Ti、AlNi、Ti3AlC2And intermetallic compounds and TiC ceramic reinforcing phase, and the hardness, the wear resistance and the corrosion resistance are improved.
The magnesium-based composite material adopts the matrix material of magnesium alloy; the transition layer material is Al powder (200-500 meshes); the protective layer material is Al powder (200-500 meshes), Ti powder (200-500 meshes) and Ni/C powder (nickel-coated carbon) (200-500 meshes).
The base material is preferably AZ91D magnesium alloy.
The magnesium-based composite material based on gradient cladding is prepared by the following method:
(1) preparing a matrix: polishing the surface of the magnesium alloy by using 600-1000-mesh sand paper to remove an oxide film on the surface, cleaning the surface by using alcohol, and airing for later use;
(2) powder mixing: mixing Al, Ti and Ni/C powder uniformly by using a ball mill, and setting parameters as follows: the stirring speed is 200-300 r/min, and the stirring time is 15-30 min;
the Al powder, the Ti powder and the Ni/C powder respectively comprise the following components in percentage by mass: 60-90% of Al, 7.6-30.4% of Ti, 1.4-5.6% of Ni and 1-4% of C;
(3) adhesive selection: uniformly mixing water glass and distilled water to serve as an adhesive, wherein the volume ratio of the water glass to the distilled water is 1: 1;
(4) preparing a gradient coating: firstly, coating Al powder on the surface of a matrix by using an adhesive, airing, carrying out laser cladding treatment to prepare a transition layer, then coating the uniformly mixed Al-Ti-Ni/C powder on the surface of the transition layer, airing, carrying out cladding treatment to prepare a protective layer, and finally forming a gradient coating on the surface of the magnesium alloy.
The powder in the step (4) adopts a preset mode, and the preset thickness of the transition layer Al powder is 0.3-0.8 mm, preferably 0.3-0.6 mm, and further preferably 0.5 mm; the preset thickness of the Al-Ti-Ni/C mixed powder of the protective layer is 0.3-0.6 mm, preferably 0.3-0.5 mm, and further preferably 0.4 mm.
The laser in the step (4) adopts Nd: YAG solid laser, which is characterized in that the absorption rate of the laser (with the wavelength of 1.06 mu m) generated by the Nd: YAG laser is obviously higher than that of CO2Laser generated by laser (wavelength 10.6 μm), mainThe parameters are preferably 3-5 ms of pulse width, 15-20 Hz of frequency, 1.0-1.5 mm of spot diameter, 120-200A of current, 90-150 mm/min of scanning speed and 40-70% of lap joint rate, and Ar is blown laterally and synchronously to protect the molten pool, and the flow rate is 5-10L/min.
The invention has the beneficial effects that:
the invention adopts a pulse Nd-YAG solid laser, uses small-parameter cladding Al powder as a transition layer on the surface of magnesium alloy, and then adjusts the parameters to increase the power to clad Al-Ti-Ni/C powder as a protective layer, thus preparing the magnesium-based gradient cladding composite material. The metallurgical bonding among the prepared material substrate, the transition layer and the protective layer is good, the heat affected zone of the substrate is small, the cladding layer is compact and has no cracks, a large amount of ceramic and intermetallic compound reinforcing phases are generated in the protective layer in situ, so that the hardness is greatly increased, the corrosion resistance is obviously improved, and the magnesium alloy substrate can be well protected when the magnesium alloy substrate is used under the corrosion and abrasion conditions.
Drawings
FIG. 1 is a cross-sectional scan of a magnesium-based gradient cladding composite material prepared in example 1.
Fig. 2 shows microstructures (a transition layer and b protective layer) of the magnesium-based gradient cladding composite material prepared in example 1.
Fig. 3 is a surface layer XRD pattern of magnesium-based gradient cladding composite material prepared in example 1.
FIG. 4 is a hardness profile of the magnesium-based gradient cladding composite material prepared in example 1.
FIG. 5 is a polarization curve diagram of a cladding layer of the magnesium-based gradient cladding composite material prepared in example 1.
Fig. 6 shows microstructures (a transition layer and b protective layer) of the mg-based gradient cladding composite prepared in example 2.
Fig. 7 is a hardness curve diagram of the magnesium-based gradient cladding composite material prepared in example 2.
FIG. 8 is a polarization curve diagram of a cladding layer of the magnesium-based gradient cladding composite material prepared in example 2.
FIG. 9 shows the protective layer microstructure of the magnesium-based gradient cladding composite prepared in example 3.
Fig. 10 is a surface layer XRD pattern of magnesium-based gradient cladding composite material prepared in example 3.
Fig. 11 is a hardness curve diagram of the magnesium-based gradient cladding composite material prepared in example 3.
FIG. 12 is a polarization curve diagram of a cladding layer of the magnesium-based gradient cladding composite material prepared in example 3.
FIG. 13 shows the protective layer microstructure of the magnesium-based gradient cladding composite prepared in example 4.
Fig. 14 is a hardness curve diagram of the magnesium-based gradient cladding composite material prepared in example 4.
Detailed Description
The following examples are illustrative and are not intended to provide any limitation on the invention. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
The materials selected in the following examples were: AZ91D magnesium alloy, Al powder (300 mesh), Ti powder (300 mesh), Ni/C powder (300 mesh) (nickel-coated carbon: 60wt.% Ni +40wt.% C), water glass, absolute ethanol, argon (purity 99.99%). The equipment used was: LMY400Nd＋YAG multifunctional solid laser.
Example 1
The AZ91D magnesium alloy is cut into blocks of 15mm multiplied by 4mm, the surface is polished by 800-mesh sand paper, the surface oxidation film is removed, then the surface is cleaned by absolute ethyl alcohol, and the blocks are dried for standby.
A mixture of water glass and distilled water in a ratio of 1:1 is selected as an adhesive, Al powder and the adhesive are mixed and stirred uniformly to form a paste, the paste is uniformly coated on the surface of a magnesium alloy substrate, the coating thickness is 0.5mm, and the paste is placed at room temperature for 24 hours and dried.
Using LMY400Nd＋YAG multifunctional pulse solid laser cladding powder precoated on the surface of magnesium alloy, wherein the cladding parameters are that the diameter of a light spot is 1.3mm, the current is 130A, the pulse width is 4ms, the frequency is 18Hz, the scanning speed is 120mm/min, and the lap joint rate is 50%. In the cladding process, argon is used as shielding gas and blown to a cladding area laterally to prevent air from invading and prevent the cladding layer from being oxidized, and the flow rate of the used gas is 7L/min is the same as the formula (I). And preparing an Al transition layer on the magnesium alloy after cladding.
Stirring and mixing Al powder, Ti powder and Ni/C powder uniformly by using a ball mill, wherein the mass ratio of Al to Ti to Ni to C in the mixed powder is 90: 7.6: 1.4: 1, the rotating speed of the ball mill is 250 r/min, and the stirring time is 20 min.
And brushing oxide and other dirt on the surface of the prepared Al transition layer by a steel wire brush, and polishing by abrasive paper. And stirring the uniformly mixed Al + Ti + Ni/C powder and the adhesive to form a paste, uniformly coating the paste on the prepared Al transition cladding layer with the coating thickness of 0.4mm, and standing at room temperature for 24 hours for airing.
And carrying out laser cladding on the secondarily precoated mixed powder by adopting the laser to prepare the protective layer. Except for the diameter of a light spot and the current, the laser cladding parameters are the same as the parameters for cladding the transition layer in pulse width, frequency, scanning speed, overlapping rate and gas flow. The diameter of the light spot is adjusted to be 1.2mm, the current is increased to 150A, and the serious evaporation of the laser and the magnesium matrix due to the direct action of the laser and the magnesium matrix is avoided due to the existence of the Al transition layer, so that the laser power can be properly increased when the protective layer is prepared, and the high-melting-point powder is completely melted.
And (3) observing and analyzing the microstructure of the magnesium-based composite material prepared by gradient cladding by using a scanning electron microscope. The test piece is cut along the thickness direction, and is respectively ground and polished by 240-mesh, 600-mesh, 800-mesh, 1500-mesh, 2000-mesh and 3000-mesh water sandpaper, and is corroded by a 4% hydrofluoric acid alcohol solution for 12 s. The cross-sectional tissue morphology of the sample is shown in FIG. 1. After the gradient cladding, the average thickness of the cladding layer is about 650 mu m, the boundary between layers is obvious, the matrix and the transition layer, the transition layer and the protective layer are in good metallurgical bonding, and the coating is compact and has no cracks. The enlarged microstructure of the transition layer and the protective layer are shown in fig. 2a and 2 b. The transition layer is mainly composed of solid solution of Al and Mg and intermetallic compound, and the protective layer is added with Ti and Ni/C to generate a large amount of white particle phase.
XRD test analysis is carried out on the surface layer of the prepared magnesium-based gradient cladding composite material, the target material is a Cu target, the scanning speed is 3 DEG/min, the scanning angle is 20 DEG-80 DEG, the result is shown in figure 3, and the matrix in the protective layer mainly comprises α -Al and Al3Mg2The particle phase is Al3A mixture of Ti and AlNi.
The hardness distribution of the magnesium-based gradient cladding composite material along the thickness direction is measured, a DHV-1000 microhardness meter is adopted, the load is 0.98N, the duration is 15s, and the result is shown in figure 4. The hardness of the magnesium alloy substrate is about 60HV, the hardness is increased in a gradient manner after gradient cladding, the average hardness of the protective layer is 280HV, and compared with the substrate, the hardness of the protective layer is increased by about 4.7 times.
FIG. 5 is a polarization curve diagram of a magnesium-based gradient cladding composite cladding layer. The test adopts CHI604E electrochemical workstation, the scanning speed is 1mV/s, the scanning range is-2V to-0.4V, and the corrosive liquid is 3.5% NaCl solution. As can be seen from the polarization curve, the self-corrosion potential of the AZ91D magnesium alloy is-1.49V, the self-corrosion potential of the magnesium-based composite material after gradient cladding is-1.101V,E corrincreased 389 mV; meanwhile, the self-corrosion current density is from 1.066 multiplied by 10-4Reduced to 3.564 × 10-5A/cm2A reduction of about 1 order of magnitude.E corrIs increased andJ corr the reduction shows that the corrosion resistance of the composite material after the gradient cladding is greatly improved. In addition, the polarization curve also shows that the melting coating layer is obviously passivated, and a compact passivation film further delays the corrosion speed and improves the corrosion resistance.
Example 2
And cutting, grinding and cleaning the AZ91D magnesium alloy according to the method in the embodiment 1, precoating 0.5mm paste Al powder on the magnesium alloy by using an adhesive, airing, and carrying out laser cladding by using the method and parameters in the embodiment 1 to prepare the Al transition layer.
Pre-coating Al, Ti and Ni/C mixed powder on an Al transition layer by using an adhesive, wherein the coating thickness is 0.4mm, the mass ratio of Al to Ti to Ni to C is 80: 15.2: 2.8: 2, and carrying out laser cladding by using the method and the parameters in the embodiment 1 to prepare the protective layer.
The prepared magnesium-based gradient cladding composite material is subjected to microstructure analysis, XRD, hardness and electrochemical test, and the parameters used by each test method are the same as those in example 1.
The microstructure morphology of the gradient cladding magnesium-based composite material is shown in fig. 6, wherein fig. 6a is a transition layer structure, and fig. 6b is a protective layer structure. The transition layer is still based on solid solution and intermetallic compound of Al and Mg, the microstructure of the protective layer is similar to that of the example 1 (FIG. 2 b), but the amount and size of the white particle phase are increased compared with the example 1 (FIG. 2 b) because the amount of Ti, Ni and C is increased.
The protective layer XRD pattern analysis result of the Mg-based composite material is similar to that of figure 3, and the matrix in the protective layer is mainly α -Al and Al3Mg2The particle phase is Al3A mixture of Ti and AlNi.
The hardness distribution of the composite material in the thickness direction is shown in fig. 7. After the gradient cladding, the hardness is also increased in a gradient manner, the average hardness of the protective layer is 290HV, and compared with the base body, the hardness of the protective layer is improved by about 4.8 times.
FIG. 8 is a polarization curve diagram of a magnesium-based gradient cladding composite cladding layer. Compared with AZ91D magnesium alloy, the self-corrosion potential is improved by 453mV, and the self-corrosion current density is from 1.066 multiplied by 10-4Reduced to 3.732 × 10-5A/cm2And the melting coating layer is obviously passivated, which shows that the corrosion speed is reduced and the corrosion resistance is greatly improved after the gradient cladding.
Example 3
And cutting, grinding and cleaning the AZ91D magnesium alloy according to the method in the embodiment 1, precoating 0.5mm paste Al powder on the magnesium alloy by using an adhesive, airing, and carrying out laser cladding by using the method and parameters in the embodiment 1 to prepare the Al transition layer.
Pre-coating Al, Ti and Ni/C mixed powder on an Al transition layer by using an adhesive, wherein the coating thickness is 0.4mm, the mass ratio of Al to Ti to Ni to C is 70: 22.8: 4.2: 3, and carrying out laser cladding by using the method and the parameters of the embodiment 1 to prepare the protective layer.
The prepared magnesium-based gradient cladding composite material is subjected to microstructure analysis, XRD, hardness and electrochemical test, and the parameters used by each test method are the same as those in example 1.
The structure of the transition layer of the gradient cladding magnesium-based composite material is similar to that of the transition layer of the example 1 and the example 2, and the microstructure appearance of the protective layer is shown in figure 9. A large number of polygonal, elongated and small number of diamond-shaped massive particles are generated in the protective layer, and the size and number of the particle phase are greatly increased compared with those of example 1 (fig. 2 b) and example 2 (fig. 6 b) because the addition amounts of Ti, Ni and C are continuously increased.
The protective layer XRD pattern analysis result of the mg-based composite material is shown in fig. 10. The matrix structure in the protective layer is Al12Mg17The particulate phase containing Al3Ti、MgNi2TiC and ternary intermetallic compound Al18Ti2Mg3、Ti3AlC2。
The hardness distribution of the composite material in the thickness direction is shown in fig. 11. The average hardness of the protective layer is 321HV, which is about 5.4 times higher than that of the substrate.
Fig. 12 is a polarization curve diagram of a magnesium-based gradient cladding composite cladding layer. Compared with AZ91D magnesium alloy, the self-corrosion potential is improved by 512mV, and the self-corrosion current density is from 1.066 multiplied by 10-4Reduced to 4.44 × 10-5A/cm2Although thoughJ corrThe increase compared to example 1 and example 2, but still much lower than AZ91D, indicates a greater improvement in corrosion resistance.
Example 4
Example 4 the methods and parameters for preparing the Al transition layer and the protective layer were the same as those of example 1, except that the ratio of the Al, Ti, Ni/C mixed powder used in the protective layer was changed, and the mass ratio of Al, Ti, Ni, and C was adjusted to 60: 30.4:5.6: 4.
The prepared magnesium-based gradient cladding composite material is subjected to microstructure analysis, XRD, hardness and electrochemical test, and the parameters used by each test method are the same as those in example 1.
The microstructure morphology of the protective layer of the gradient cladding magnesium-based composite material is shown in fig. 13. The number of polygonal particle phases was further increased as compared with example 3 (fig. 9), and the elongated particle phases were changed into elliptical shapes, both in number and size.
The protective layer XRD test analysis result of the mg-based composite material showed that the kind of the phases in the cladding layer was the same as that of example 3, and only the specific contents of the phases were different.
The hardness distribution of the composite material in the thickness direction is shown in fig. 14. The average hardness of the protective layer is 347HV, the maximum hardness is 481HV, which is about 8 times of that of the base body, and the hardness of the cladding layer is further improved.
The polarization curve of the cladding layer also shows that the self-corrosion potential is increased by 477mV compared with AZ91D, and the self-corrosion current density is reduced to 9.377X 10-5A/cm2Albeit fromJ corrThe corrosion rate is limited from the viewpoint of (1), but the corrosion resistance is still significantly improved as compared with the magnesium alloy.

Claims (10)

1. The magnesium-based composite material based on gradient cladding is characterized in that: the magnesium-based composite material takes magnesium alloy as a matrix, adopts the laser cladding technology to carry out gradient cladding on the magnesium alloy matrix, firstly cladding Al powder as a transition layer, and continuously cladding Al-Ti-Ni/C mixed powder as a protective layer.
2. The gradient cladding-based magnesium-based composite material of claim 1, wherein: the Al powder of the transition layer material is 200-500 meshes; the protective layer material Al powder is 200-500 meshes, the Ti powder is 200-500 meshes, and the nickel-coated carbon Ni/C powder is 200-500 meshes.
3. The gradient cladding-based magnesium-based composite material of claim 2, wherein: in the protective layer, the mass percentages of the components are respectively as follows: 60 to 90 percent of Al, 7.6 to 30.4 percent of Ti, 1.4 to 5.6 percent of Ni and 1 to 4 percent of C.
4. The gradient cladding-based magnesium-based composite material of claim 1, wherein: the base material is AZ91D magnesium alloy.
5. The preparation method of the magnesium-based composite material based on gradient cladding, which is characterized by comprising the following steps: the method comprises the following steps:
(1) preparing a matrix: polishing the surface of the magnesium alloy by using 600-1000-mesh sand paper to remove an oxide film on the surface, cleaning the surface by using alcohol, and airing for later use;
(2) powder mixing: uniformly mixing Al powder, Ti powder and Ni/C powder by using a ball mill, wherein the mass percentages of the components in the Al powder, the Ti powder and the Ni/C powder are respectively as follows: 60-90% of Al, 7.6-30.4% of Ti, 1.4-5.6% of Ni and 1-4% of C;
(3) adhesive selection: uniformly mixing water glass and distilled water in a volume ratio of 1:1 to obtain a binder;
(4) preparing a gradient coating: firstly, coating Al powder on the surface of a matrix in a paste form by using an adhesive, and carrying out laser cladding treatment after airing to prepare a transition layer; and then coating the uniformly mixed Al-Ti-Ni/C powder on the surface of the transition layer by using an adhesive, airing, carrying out cladding treatment to prepare a protective layer, and finally forming a gradient coating on the surface of the magnesium alloy.
6. The preparation method of magnesium-based composite material based on gradient cladding as claimed in claim 5, wherein: setting parameters in the mixing process in the step (2): the stirring speed is 200-300 r/min, and the stirring time is 15-30 min.
7. The preparation method of magnesium-based composite material based on gradient cladding as claimed in claim 5, wherein: and (4) adopting a preset mode for the powder in the step (4), wherein the preset thickness of the transition layer Al powder is 0.3-0.8 mm, and the preset thickness of the protective layer Al-Ti-Ni/C mixed powder is 0.3-0.6 mm.
8. The preparation method of magnesium-based composite material based on gradient cladding as claimed in claim 7, wherein: the preset thickness of the Al powder is 0.3-0.6 mm, and the preset thickness of the Al-Ti-Ni/C mixed powder is 0.3-0.5 mm.
9. The preparation method of magnesium-based composite material based on gradient cladding as claimed in claim 5, wherein: the laser in the step (4) adopts Nd: YAG solid laser, Nd: YAG laser generates laser wavelength of 1.06 μm.
10. The preparation method of magnesium-based composite material based on gradient cladding as claimed in claim 9, wherein: nd: parameters of the YAG solid laser are as follows: the pulse width is 3-5 ms, the frequency is 15-20 Hz, the spot diameter is 1.0-1.5 mm, the current is 120-200A, the scanning speed is 90-150 mm/min, the lap joint rate is 40-70%, the Ar protection molten pool is blown laterally and synchronously, and the flow rate is 5-10L/min.
CN201911333231.3A 2019-12-23 2019-12-23 Magnesium-based composite material based on gradient cladding and preparation method thereof Pending CN111088485A (en)

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Cited By (1)

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Publication number Priority date Publication date Assignee Title
CN114507853A (en) * 2022-01-25 2022-05-17 济南森峰激光科技股份有限公司 Laser cladding preparation method of magnesium alloy surface gradient ceramic composite coating

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