CN111962017A - Method for preparing high-hardness metal layer on surface of magnesium alloy - Google Patents
Method for preparing high-hardness metal layer on surface of magnesium alloy Download PDFInfo
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- CN111962017A CN111962017A CN202010863957.4A CN202010863957A CN111962017A CN 111962017 A CN111962017 A CN 111962017A CN 202010863957 A CN202010863957 A CN 202010863957A CN 111962017 A CN111962017 A CN 111962017A
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- 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
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- C23C10/00—Solid state diffusion of only metal elements or silicon into metallic material surfaces
- C23C10/28—Solid state diffusion of only metal elements or silicon into metallic material surfaces using solids, e.g. powders, pastes
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- C23C10/36—Embedding in a powder mixture, i.e. pack cementation only one element being diffused
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Abstract
The invention discloses a method for preparing a high-hardness metal layer on the surface of a magnesium alloy, which comprises the steps of placing the magnesium alloy subjected to surface treatment into a pressure container filled with zinc powder, coating the magnesium alloy with the zinc powder, heating the pressure container to 370-395 ℃ under the pressure condition of 5-30 MPa, preserving heat for 50-180 min, and naturally cooling to room temperature after the heat preservation is finished, thus preparing the high-hardness metal layer on the surface of the magnesium alloy. Compared with the prior art, the method has the advantages that the temperature is low, the reaction condition is easier to control, the diffusion time is short, the production efficiency is improved, the hardness of the prepared metal layer is high, and the bonding force with the magnesium alloy is strong.
Description
Technical Field
The invention belongs to the technical field of magnesium alloy surface strengthening, and particularly relates to a method for preparing a high-hardness metal layer on the surface of a magnesium alloy.
Background
The magnesium alloy has a series of advantages of light weight, high specific strength, good electromagnetic shielding property and the like, is widely applied to the fields of automobiles, 3C and aerospace, is known as a green engineering material in the 21 st century, but is not corrosion-resistant, wear-resistant and the like, so that the mass use of the magnesium alloy is restricted. In recent years, many scholars adopt technologies such as anodic oxidation, micro-arc oxidation, vapor deposition treatment, surface spraying, electroplating, in-situ synthesis and the like to improve the wear resistance and corrosion resistance of the magnesium alloy. However, the surface film formed by the techniques of surface spraying, micro-arc oxidation, electroplating, etc. often has a weak bonding force with the substrate, and the discussion of the process parameters is time-consuming.
The Chinese patent 201410025270.8 discloses a method for alloying the surface of magnesium alloy by using solid-state thermal diffusion technology, which comprises the steps of burying a pure magnesium or magnesium alloy workpiece subjected to surface treatment into an iron tank containing pure zinc powder for compaction, and then putting the iron tank into a heating furnace for heating, wherein the heating temperature is 400-470 ℃, and the heating time is 4-20 h. The method gets rid of the problems of long heat treatment time, overhigh temperature and low industrial production efficiency of thermal diffusion zinc infiltration under the vacuum or inert gas protection condition, and according to a Mg-Zn binary phase diagram shown in figure 1, when the temperature reaches 325 ℃, phase change occurs, and the phase change stays above the phase change temperature of 400-470 ℃ for a long time, so that various intermetallic compounds in an infiltration layer are easy to grow, the performance of the infiltration layer is reduced, different intermetallic compounds are decomposed, and a large amount of shrinkage porosity and shrinkage holes are left in the infiltration layer.
Disclosure of Invention
In view of the above-mentioned disadvantages of the prior art, the present invention aims to provide a method for preparing a high-hardness metal layer on the surface of a magnesium alloy, which has the advantages of low temperature, high production efficiency, high hardness of the prepared metal layer, and strong bonding force with the magnesium alloy.
A method for preparing a high-hardness metal layer on the surface of a magnesium alloy comprises the steps of placing the magnesium alloy subjected to surface treatment in a pressure container filled with zinc powder, coating the magnesium alloy with the zinc powder, heating the pressure container to 370-395 ℃ under the pressure condition of 5-30 MPa, preserving heat for 50-180 min, and naturally cooling to room temperature after heat preservation is finished, so that the high-hardness metal layer is prepared on the surface of the magnesium alloy.
Further, the magnesium alloy surface treatment process comprises the following steps: firstly, grinding the magnesium alloy by adopting metallographic abrasive paper of 600#, 800# and 1500# in sequence to remove an oxide film on the surface of the magnesium alloy; and then, putting the magnesium alloy into an acetone solution or an industrial degreasing agent for ultrasonic treatment for 3-5 min, and then cleaning and drying the magnesium alloy by using deionized water to obtain the magnesium alloy after surface treatment.
Further, during charging, the magnesium alloy subjected to surface treatment is placed in a pressure container, the magnesium alloy is coated with zinc powder, and then the pressure container is pressurized, so that the pressure in the pressure container is maintained at 5-30 MPa.
Furthermore, the pressure container comprises a cylindrical pipe and end sockets which are arranged at two ends of the cylindrical pipe and can be inserted into the two ends of the cylindrical pipe to seal the two ends of the cylindrical pipe, a pressure plate which is axially vertical to the cylindrical pipe is arranged at the outer side end of each end socket, and a plurality of bolt holes are formed in the pressure plate; the magnesium alloy is arranged in the cylindrical pipe, zinc powder is arranged in the cylindrical pipe to coat the magnesium alloy, then the end socket is compressed from the outer side to the inside of the cylindrical pipe, the pressure in the cylindrical pipe is 5-30 MPa, and then a plurality of bolts sequentially penetrate through the two corresponding bolt holes in the two pressing plates to fixedly connect the two pressing plates, so that the pressure in the cylindrical pipe is maintained at 5-30 MPa.
Furthermore, the granularity of the zinc powder is 800-2000 mu m, and the purity is more than 98.5%.
Further, when the pressure container is heated, the heating rate is 10-20 ℃/min.
Compared with the prior art, the invention has the following beneficial effects:
1. the method has the advantages of low diffusion temperature, easy control of conditions in the process of preparing the metal layer, short diffusion time, contribution to improving the production efficiency and contribution to industrial application.
2. The metal layer prepared by the invention only contains the intermetallic compound Mg7Zn3Or MgZn, Mg7Zn3The metallurgical bonding between the metal layer and the magnesium alloy substrate is realized, and the bonding force between the metal layer and the magnesium alloy substrate is improved.
3. The metal layer prepared by the method has a compact structure, and the average microhardness of the metal layer reaches 160-222 HV0.2Compared with the common magnesium alloy, the wear resistance of the magnesium alloy can be improved by 3-6 times, and the wear resistance of the magnesium alloy is effectively improved.
Drawings
FIG. 1-Mg-Zn binary phase diagram.
Fig. 2-schematic structural view of a pressure vessel.
FIG. 3-SEM image of the metal layer prepared in example 1.
FIG. 4-X-ray diffraction pattern of the metal layer prepared in example 1.
FIG. 5-microhardness profile of the metal layer prepared in example 1.
FIG. 6-Tafel plot of the galvanic corrosion of the metal layer prepared in example 1.
FIG. 7-SEM micrograph of metal layer prepared in comparative example 1.
Figure 8-microhardness indentation pattern prepared in example 2.
Figure 9-microhardness indentation patterns prepared in example 3.
Detailed Description
The present invention will be described in further detail with reference to the accompanying drawings and specific embodiments.
A method for preparing a high-hardness metal layer on the surface of a magnesium alloy comprises the steps of placing the magnesium alloy subjected to surface treatment in a pressure container filled with zinc powder, coating the magnesium alloy with the zinc powder, heating the pressure container to 370-395 ℃ under the pressure condition of 5-30 MPa, preserving heat for 50-180 min, and naturally cooling to room temperature after heat preservation is finished, so that the high-hardness metal layer is prepared on the surface of the magnesium alloy.
Under the condition of pressurization, the quantity of zinc atoms attached to the surface of the magnesium alloy is increased, and meanwhile, the transition distance of the zinc atoms to the magnesium alloy is reduced to a certain extent, so that the effective collision quantity of Mg atoms and Zn atoms is increased, and the reduction of the diffusion temperature and the diffusion time is facilitated.
In addition, the magnesium alloy and the Zn powder are placed in the pressure container, the diffusion temperature is 370-395 ℃, the energy obtained by Zn atoms cannot break through the grain boundary barrier of the pressure container, only the grain boundary gap of the low-melting-point magnesium alloy is enlarged, the replacement reaction is easier to occur, and the original disordered and diffused Zn atoms are easier to diffuse along the direction of the magnesium alloy under the pressure condition. Specifically, under the condition of no pressure, the Zn atoms are subjected to disordered diffusion, a large part of the Zn atoms are not diffused towards the magnesium alloy, and under the pressure condition, the pressure is used for guiding the Zn atoms subjected to disordered diffusion, so that more Zn atoms are diffused towards the magnesium alloy, and more Zn atoms enter the magnesium alloy matrix in the same time, thereby being beneficial to saving diffusion time.
Under the pressure condition of 5-30 MPa, the release of the internal stress of the magnesium alloy cannot be influenced after heat treatment, so that the cooled phases are compact, and no gap is formed. The reason is as follows: in this pressure range, the pressure only serves to reduce the diffusion distance and guidance. At the above diffusion temperatures, the internal stresses drive the plastic deformation of the material until the internal stresses are at equilibrium with the yield stress at that stress. If the pressure is too large, the yield stress is relatively increased, after the pressure is restored to room temperature and an external pressure maintaining device is removed, the yield stress is reduced, the balance between the internal stress and the yield stress is broken, and the defects of cracks, shrinkage porosity and the like of a sample are easily caused.
In specific implementation, the magnesium alloy surface treatment process comprises the following steps: firstly, grinding the magnesium alloy by adopting metallographic abrasive paper of 600#, 800# and 1500# in sequence to remove an oxide film on the surface of the magnesium alloy; and then, putting the magnesium alloy into an acetone solution or an industrial degreasing agent for ultrasonic treatment for 3-5 min, and then cleaning and drying the magnesium alloy by using deionized water to obtain the magnesium alloy after surface treatment.
In the specific implementation, during charging, the magnesium alloy after surface treatment is placed in a pressure container, zinc powder is used for coating the magnesium alloy, and then the pressure container is pressurized, so that the pressure in the pressure container is maintained at 5-30 MPa.
Referring to fig. 2, the pressure container comprises a cylindrical tube 1 and end sockets 2 which are arranged at two ends of the cylindrical tube 1 and can be inserted into two ends of the cylindrical tube 1 to seal the two ends of the cylindrical tube 1, a pressure plate 3 which is axially vertical to the cylindrical tube is arranged at the outer side end of the end socket 2, and a plurality of bolt holes are arranged on the pressure plate 3; the magnesium alloy is arranged in the cylindrical pipe, zinc powder is arranged in the cylindrical pipe to coat the magnesium alloy, then the end socket is compressed from the outer side to the inner side of the cylindrical pipe, the pressure in the cylindrical pipe is 5-30 MPa, and then the bolts 4 sequentially penetrate through the two corresponding bolt holes in the two pressing plates to fixedly connect the two pressing plates, so that the pressure in the cylindrical pipe is maintained at 5-30 MPa.
In the specific implementation, the granularity of the zinc powder is 800-2000 mu m, and the purity is more than 98.5%.
When in use, the zinc powder is prevented from being oxidized. The smaller the particle size of the Zn powder, the more easily the Zn atom absorbs energy, i.e., the more easily the transition occurs, and the more easily the diffusion occurs. Meanwhile, because elements such as Fe, Cu and the like have toxic action on magnesium, the performance of the magnesium alloy is reduced rapidly, and the purity requirement of the zinc powder used for diffusion is high.
In specific implementation, when the pressure container is heated, the heating rate is 10-20 ℃/min.
Example 1
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 5min, cleaning a workpiece with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 800 mu m, and pressurizing the container by using a press machine to keep the pressure in the container at 5 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 15 ℃/min, heating to 390 ℃, then preserving heat for 120min, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
This example is on the surface of magnesium alloyThe prepared metal layer is compact and uniform, the appearance is bright, the hand feeling is round and smooth, the scanning electron microscope tissue diagram, the X-ray diffraction pattern, the microhardness distribution diagram and the electrochemical tafel curve diagram are respectively shown in fig. 3, fig. 4, fig. 5 and fig. 6, and as can be seen from fig. 3, the metal layer is embedded into the magnesium alloy matrix, is well combined with the AZ31 magnesium alloy matrix, and is compact and free of holes; as can be seen from FIG. 4, the zinc element penetrated into the matrix structure and formed the intermetallic compound Mg7Zn3And MgZn; as can be seen from FIG. 5, the hardness of the metal layer was increased by about 5.6 times as compared with that of the AZ31 magnesium alloy substrate, and the average hardness of the intermetallic compound of the metal layer was 222HV0.2The hardness of the AZ31 magnesium alloy can be effectively improved by the metal layer prepared by the hot solid state pressure-maintaining diffusion zinc impregnation; as can be seen from FIG. 6, the corrosion potential shifted positively by 0.05V, which indicates that the corrosion tendency of the metal layer is reduced, and the corrosion current densities of the substrate and the metal layer are respectively 1.732X 10 by calibrating with Chenghua 660E-4(A.cm-2) And 8.253 × 10-5(A.cm-2) The corrosion current of the metal layer is reduced by half order of magnitude, which shows that the corrosion resistance of the metal layer obtained after the surface of the magnesium alloy is subjected to zinc impregnation is enhanced.
Comparative example 1
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 5min, cleaning a workpiece with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 800 mu m, and pressurizing the container by using a press machine to keep the pressure in the container at 5 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 15 ℃/min, heating to 390 ℃, then preserving heat for 240min, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
In this embodiment, a scanning electron microscope scanning image of the metal layer prepared on the surface of the magnesium alloy is shown in fig. 7, and the metal layer has a net structure and many non-dense gaps. And the intermetallic compound in the metal layer in the present embodiment includes MgZn (at a in fig. 7), Mg7Zn3(at B in FIG. 7) and MgZn2(at C in FIG. 7), in this example, coarse Mg was produced as compared with example 17Zn3Phase and MgZn2Phase, whereby the metal layer becomes a network structure, and MgZn phase, Mg7Zn3Phase and MgZn2There are voids between the phases, making the metal layer less dense.
Example 2
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 5min, cleaning with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 1000 microns, and pressurizing the container by using a press machine to keep the pressure in the container at 10 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 15 ℃/min, heating to 390 ℃, then preserving heat for 90min, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
In this example, the metal layer prepared on the surface of the magnesium alloy is dense and uniform, has bright appearance, smooth hand feeling and excellent wear resistance, and the microhardness of the substrate layer and the metal layer in this example is measured by a microindenter, and the result is shown in fig. 8, where the average microhardness of the metal layer is 194.1HV0.2And bonded well to the magnesium alloy substrate, and the metal layer contained only Mg according to the X-ray diffraction pattern of the metal layer of this example7Zn3And (4) phase(s).
Example 3
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 3min, cleaning a workpiece with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 800 mu m, and pressurizing the container by using a press machine to keep the pressure in the container at 15 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 20 ℃/min, heating to 380 ℃, then preserving heat for 90min, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
In this example, the metal layer prepared on the surface of the magnesium alloy was dense and uniform and had a bright appearance, but coarse lamellar layers began to appear in the infiltrated layer, and the microhardness of the substrate layer and the metal layer in this example was measured by a microindentation machine, and the result is shown in FIG. 9, in which the average microhardness was 168.1HV0.2And bonded well to the magnesium alloy substrate, and the metal layer contained only Mg according to the X-ray diffraction pattern of the metal layer of this example7Zn3And (4) phase(s).
Example 4
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 5min, cleaning a workpiece with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 800 mu m, and pressurizing the container by using a press machine to keep the pressure in the container at 5 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 15 ℃/min, keeping the temperature for 60min after heating to 395 ℃, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
The metal layer prepared on the surface of the magnesium alloy in the embodiment is compact and uniform, has bright appearance, mellow hand feeling and excellent wear resistance, and the average microhardness is 188.6HV0.2And bonded well to the magnesium alloy substrate, and the metal layer contained only Mg according to the X-ray diffraction pattern of the metal layer of this example7Zn3And (4) phase(s).
Example 5
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 3min, cleaning a workpiece with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 2000 mu m, and pressurizing the container by using a press machine to keep the pressure in the container at 15 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 20 ℃/min, heating to 390 ℃, then preserving heat for 120min, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
In the embodiment, the metal layer prepared on the surface of the magnesium alloy is compact and uniform and has bright appearance, but coarse lamellar layers begin to appear in the penetration layer, and the average microhardness is 168.1HV0.2And bonded well to the magnesium alloy substrate, and the metal layer contained only Mg according to the X-ray diffraction pattern of the metal layer of this example7Zn3And (4) phase(s).
Example 6
(1) Cutting an AZ31 magnesium alloy sample into round slices with phi 20mm multiplied by 5mm, and grinding by using metallographic abrasive paper of No. 600, No. 800 and No. 1500 one by one to remove an oxide film on the surface of the magnesium alloy;
(2) putting the polished sample into an acetone solution for ultrasonic treatment for 3min, cleaning a workpiece with deionized water, and finally blowing the sample dry with a blower;
(3) putting the blow-dried magnesium alloy sample into a container, wrapping the sample with zinc powder, wherein the granularity of the zinc powder is 1000 microns, and pressurizing the container by using a press machine to keep the pressure in the container at 10 MPa;
(4) placing the pressure-maintaining container in a heating furnace for heating, wherein the heating rate is 10 ℃/min, heating to 370 ℃, then preserving heat for 180min, and then cooling along with the furnace, namely preparing a high-hardness metal layer on the surface of an AZ31 magnesium alloy sample;
(5) and polishing the magnesium alloy sample subjected to the thermal diffusion treatment.
The metal layer prepared on the surface of the magnesium alloy in the embodiment is compact and uniform, has bright appearance, mellow hand feeling and excellent wear resistance, and the average microhardness is 180.5HV0.2And bonded well to the magnesium alloy substrate, and the metal layer contained only Mg according to the X-ray diffraction pattern of the metal layer of this example7Zn3A phase and a MgZn phase.
Finally, it should be noted that the above-mentioned examples of the present invention are only examples for illustrating the present invention, and are not intended to limit the embodiments of the present invention. Variations and modifications in other variations will occur to those skilled in the art upon reading the foregoing description. Not all embodiments are exhaustive. All obvious changes and modifications of the present invention are within the scope of the present invention.
Claims (6)
1. A method for preparing a high-hardness metal layer on the surface of a magnesium alloy is characterized in that the magnesium alloy subjected to surface treatment is placed in a pressure container filled with zinc powder, the zinc powder coats the magnesium alloy, the pressure container is heated to 370-395 ℃ under the pressure condition of 5-30 MPa, heat preservation is carried out for 50-180 min, and after the heat preservation is finished, the magnesium alloy is naturally cooled to room temperature, so that the high-hardness metal layer is prepared on the surface of the magnesium alloy.
2. The method for preparing the high-hardness metal layer on the surface of the magnesium alloy as claimed in claim 1, wherein the magnesium alloy surface treatment process comprises: firstly, grinding the magnesium alloy by adopting metallographic abrasive paper of 600#, 800# and 1500# in sequence to remove an oxide film on the surface of the magnesium alloy; and then, putting the magnesium alloy into an acetone solution or an industrial degreasing agent for ultrasonic treatment for 3-5 min, and then cleaning and drying the magnesium alloy by using deionized water to obtain the magnesium alloy after surface treatment.
3. The method for preparing a high-hardness metal layer on the surface of a magnesium alloy as claimed in claim 1, wherein the magnesium alloy is placed in a pressure vessel after surface treatment, the magnesium alloy is coated with zinc powder, and the pressure vessel is pressurized to maintain the pressure in the pressure vessel at 5-30 MPa.
4. The method for preparing the high-hardness metal layer on the surface of the magnesium alloy as claimed in claim 3, wherein the pressure container comprises a cylindrical tube and end sockets which are arranged at two ends of the cylindrical tube and can be inserted into the two ends of the cylindrical tube to seal the two ends of the cylindrical tube, the outer end of each end socket is provided with a pressure plate which is vertical to the axial direction of the cylindrical tube, and the pressure plate is provided with a plurality of bolt holes; the magnesium alloy is arranged in the cylindrical pipe, zinc powder is arranged in the cylindrical pipe to coat the magnesium alloy, then the end socket is compressed from the outer side to the inside of the cylindrical pipe, the pressure in the cylindrical pipe is 5-30 MPa, and then a plurality of bolts sequentially penetrate through the two corresponding bolt holes in the two pressing plates to fixedly connect the two pressing plates, so that the pressure in the cylindrical pipe is maintained at 5-30 MPa.
5. The method for preparing the high-hardness metal layer on the surface of the magnesium alloy as claimed in claim 1, wherein the zinc powder has a particle size of 800 μm to 2000 μm and a purity of > 98.5%.
6. The method for preparing a high-hardness metal layer on the surface of a magnesium alloy according to claim 1, wherein the temperature rise rate is 10-20 ℃/min when the pressure vessel is heated.
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| 付晓鹏: "AZ91D镁合金表面固态铝锌共渗及铝箔包覆工艺研究", 《万方》 * |
| 程旭艳: "AZ91D镁合金固态热扩渗锌及其耐腐蚀性能研究", 《中国优秀硕士学位论文全文数据库（工程科技Ⅰ辑）》 * |
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| CN111962017B (en) | 2022-11-22 |
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