CN117026036B - High-heat-conductivity high-strength wrought magnesium alloy and preparation method thereof - Google Patents
High-heat-conductivity high-strength wrought magnesium alloy and preparation method thereof Download PDFInfo
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- 229910000861 Mg alloy Inorganic materials 0.000 title claims abstract description 49
- 238000002360 preparation method Methods 0.000 title claims abstract description 11
- 239000000956 alloy Substances 0.000 claims abstract description 80
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 78
- 238000001125 extrusion Methods 0.000 claims abstract description 47
- 239000011777 magnesium Substances 0.000 claims abstract description 46
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 21
- 239000012535 impurity Substances 0.000 claims abstract description 13
- 238000003723 Smelting Methods 0.000 claims abstract description 10
- 238000000034 method Methods 0.000 claims description 25
- 239000002994 raw material Substances 0.000 claims description 8
- 229910052684 Cerium Inorganic materials 0.000 claims description 6
- 230000001681 protective effect Effects 0.000 claims description 6
- 238000010791 quenching Methods 0.000 claims description 5
- 230000000171 quenching effect Effects 0.000 claims description 5
- 238000003756 stirring Methods 0.000 claims description 5
- 229910052746 lanthanum Inorganic materials 0.000 claims description 4
- 230000008018 melting Effects 0.000 claims description 4
- 238000002844 melting Methods 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims description 3
- 150000002910 rare earth metals Chemical class 0.000 claims description 2
- 239000007858 starting material Substances 0.000 claims 1
- 238000005275 alloying Methods 0.000 abstract description 3
- 230000000052 comparative effect Effects 0.000 description 18
- 239000011572 manganese Substances 0.000 description 18
- 229910052749 magnesium Inorganic materials 0.000 description 17
- 230000008569 process Effects 0.000 description 15
- 239000011159 matrix material Substances 0.000 description 13
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 12
- 230000000694 effects Effects 0.000 description 8
- 239000007787 solid Substances 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
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- 229910052742 iron Inorganic materials 0.000 description 5
- 239000013078 crystal Substances 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
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- 238000004891 communication Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
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- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
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Abstract
The invention discloses a high-heat-conductivity high-strength wrought magnesium alloy and a preparation method thereof, and belongs to the technical field of magnesium alloys. The high-heat-conductivity high-strength wrought magnesium alloy is an Mg-Mn-X alloy system; wherein X is a light rare earth element, the content is 0.5-5.0 wt.%, and the content of Mn is 0.5-4.0 wt.%; the balance being Mg and unavoidable impurities. According to the invention, by adding proper alloying elements, the high-heat-conductivity high-strength deformed magnesium alloy with excellent comprehensive performance can be obtained by utilizing simple alloy smelting and extrusion heat deformation, and the prepared high-heat-conductivity high-strength deformed magnesium alloy coordinates the problem that the heat conductivity and the strength of the magnesium alloy are not matched.
Description
Technical Field
The invention relates to the technical field of magnesium alloy, in particular to a high-heat-conductivity high-strength deformed magnesium alloy and a preparation method thereof.
Background
With the high-speed development of the fields of 5G communication, LED illumination, aerospace, new energy automobiles and the like, the components are highly integrated and high-power, so that the heat generated in the running process of equipment is greatly increased, and the thermal management becomes one of the bottleneck problems to be solved. Therefore, materials with high heat conductivity are required to timely conduct out redundant heat so as to ensure the stability and reliability of equipment operation, and meanwhile, the materials are required to have the characteristics of high strength, light weight and the like. The magnesium alloy is used as the lightest metal structural material in the current engineering application, the density of the magnesium alloy is only one fifth of that of copper, two thirds of that of aluminum, and the magnesium alloy has the characteristics of high specific strength, specific stiffness, excellent heat conduction performance, electromagnetic shielding performance, cutting processability and the like, and has unique advantages in the field of light high-heat-conduction high-strength materials.
The thermal conductivity of pure magnesium is high, which can reach 158W/(m.K), but the mechanical property is poor, which can not meet the requirement of industrial application. Alloying is an effective method for improving the mechanical properties of magnesium alloys, but the strength is improved, meanwhile, the heat conductivity of the magnesium alloys is obviously reduced, and good matching between the two is not achieved. The commercial magnesium alloys commonly used at present, such as AZ81, have a room temperature thermal conductivity of 51W/(m.K), a tensile strength of 275MPa, a WE43 room temperature thermal conductivity of 51W/(m.K), a tensile strength of 250MPa, and a high rare earth alloy, such as Mg-11Y-5Gd-2Zn-0.5Zr, a tensile strength of 307MPa, but a thermal conductivity of only 23W/(m.K). At present, the advantage of high heat-conducting property of the magnesium alloy is not fully exerted, and the application of the magnesium alloy in the field of heat-radiating materials is greatly limited. Therefore, developing magnesium alloy materials with high heat conductivity and high strength has great application value.
Disclosure of Invention
The invention aims to provide a high-heat-conductivity high-strength wrought magnesium alloy and a preparation method thereof.
In order to achieve the above purpose, the present invention provides the following technical solutions:
One of the technical schemes of the invention is as follows: providing a high-heat-conductivity high-strength wrought magnesium alloy, wherein the high-heat-conductivity high-strength wrought magnesium alloy is an Mg-Mn-X alloy system; wherein X is a light rare earth element, the content is 0.5-5.0 wt.%, and the content of Mn is 0.5-4.0 wt.%; the balance being Mg and unavoidable impurities.
Preferably, the light rare earth element is one or two of La and Ce.
Compared with other (light) rare earth elements, the La and Ce selected by the method have lower cost, are easy to obtain, have low solid solubility in the Mg matrix, have small influence degree on lattice distortion, and can not obviously reduce the heat conductivity of the magnesium alloy. In addition, la and Ce elements are added into the magnesium matrix, so that the magnesium matrix has stronger fine-grain strengthening and second-phase strengthening effects.
The second technical scheme of the invention is as follows: the preparation method of the high-heat-conductivity high-strength wrought magnesium alloy comprises the following steps:
(1) Preparing raw materials according to the element proportion;
(2) Preheating the raw materials, smelting in a protective atmosphere, and cooling to obtain an alloy ingot;
(3) Preparing the alloy ingot into a blank for extrusion, extruding and deforming the blank for extrusion, and carrying out cold quenching to obtain the high-heat-conductivity high-strength deformed magnesium alloy.
Preferably, the preheating in step (2) is at a temperature of 200 to 300 ℃.
Preferably, the gas of the protective atmosphere in the step (2) is a mixed gas of SF 6 and CO 2.
Preferably, the raw materials in the step (1) are pure Mg ingots, mg-Mn intermediate alloys and Mg-light rare earth element intermediate alloys.
More preferably, the specific operation of smelting in step (2) is: firstly, melting a pure Mg ingot, then adding an Mg-Mn intermediate alloy and an Mg-light rare earth element intermediate alloy, standing, preserving heat, and stirring to finish smelting; the melting temperature of the pure Mg ingot is 720-760 ℃; the standing and heat preserving time is 10-20 min; the stirring time is 3-5 min.
Preferably, the extrusion deformation in the step (3) further comprises a preheating step; the preheating temperature is 300-400 ℃ and the preheating time is 10-30 min.
Preferably, the extrusion ratio of the extrusion deformation in the step (3) is (10-25): 1, and the extrusion rate is 0.05-5 mm/s.
The beneficial technical effects of the invention are as follows:
The high-heat-conductivity high-strength wrought magnesium alloy provided by the invention coordinates the problem that the heat conductivity and the strength of the magnesium alloy are not matched, and can be obtained by adding proper alloying elements, utilizing simple alloy smelting and extrusion heat deformation. The deformation magnesium alloy prepared by the invention has tensile yield strength of 363-416 MPa, tensile strength of 379-430 MPa, elongation of 5-10%, excellent heat conduction performance, and room temperature heat conductivity of 135-141W/(m.K), can effectively meet the heat dissipation performance requirements of parts such as 5G communication, radar, LED illumination, 3C products and the like, and has wide application prospects in the fields of electronics, aerospace, automobiles and the like.
The preparation method provided by the invention has the advantages of short process flow, simple equipment requirement, easiness in operation, high preparation efficiency and lower cost, and is suitable for large-scale production.
The invention adds light rare earth elements La, ce, etc. with lower cost on the basis of Mg-Mn series alloy. Mn is an alloy element commonly used in magnesium alloy, and the addition of Mn can eliminate impurities such as Fe in the magnesium alloy and can improve the corrosion resistance of the magnesium alloy. Mn has small solid solubility in magnesium alloy, does not react with Mg, and has limited effect of improving mechanical properties of as-cast alloy. But can dynamically separate out simple substance manganese particles in the thermal deformation process to prevent dislocation movement, further refine magnesium alloy grains and improve the mechanical property of the deformed alloy. While when the Mn content is around 2wt.%, the effect on the thermal conductivity of the magnesium alloy is still small. The solid solubility of the light rare earth element in magnesium is small, the reduction degree of the heat conductivity of magnesium alloy is small, and the magnesium alloy has the functions of purifying melt, refining alloy structure and improving the mechanical properties of alloy at room temperature and high temperature. In the invention, the alloy element Mn is in a supersaturated state in the cast magnesium matrix, and the light rare earth element exists in the form of Mg-RE phase and solute atoms. In the extrusion heat deformation process, the Mg-RE phase can effectively pin the grain boundary and provide heterogeneous nucleation points to promote dynamic recrystallization, refine crystal grains of the extruded alloy and be crushed and decomposed into fine particles in the hot extrusion process, so that the light rare earth element can play roles of fine crystal strengthening, second phase strengthening and the like, and the alloy has higher strength. In addition, because the solid solubility of Mn and light rare earth elements is very low, a large amount of nanoscale second phases are dynamically precipitated in the extrusion process, and grain boundary movement can be blocked, so that the growth of recrystallized grains is inhibited. The large amount of nano dynamic precipitated phases consume solute atoms in the magnesium matrix while strengthening the alloy, so that the content of the solute atoms is greatly reduced, the degree of lattice distortion of the magnesium matrix is greatly reduced, the scattering effect on electrons and phonons in the heat conduction process is obviously weakened, and the heat conductivity of the alloy is further improved. Therefore, the magnesium alloy material prepared by the invention has high heat conduction and high strength.
The attached drawings
FIG. 1 is a metallographic structure diagram of an alloy ingot prepared in step three of example 1 of the present invention.
FIG. 2 shows the structure of a scanning electron microscope of the Mg-1.4Mn-2.3Ce alloy prepared in example 1 of the present invention.
Detailed Description
Various exemplary embodiments of the invention will now be described in detail, which should not be considered as limiting the invention, but rather as more detailed descriptions of certain aspects, features and embodiments of the invention. It is to be understood that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.
In addition, for numerical ranges in this disclosure, it is understood that each intermediate value between the upper and lower limits of the ranges is also specifically disclosed. Every smaller range between any stated value or stated range, and any other stated value or intermediate value within the stated range, is also encompassed within the invention. The upper and lower limits of these smaller ranges may independently be included or excluded in the range.
Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein can be used in the practice or testing of the present invention.
As used herein, the terms "comprising," "including," "having," "containing," and the like are intended to be inclusive and mean an inclusion, but not limited to.
Example 1
The high-heat-conductivity high-strength wrought magnesium alloy comprises the following alloy elements in percentage by mass: mn:1.4wt.%, ce:2.3wt.% and the balance of Mg and unavoidable impurities such as Fe, si, etc.
The preparation method of the high-heat-conductivity high-strength wrought magnesium alloy comprises the following steps:
Step one, raw material preparation:
The mass percentages of the elements are Mn:1.4wt.%, ce:2.3wt.% of Mg and the balance of Mg, and weighing raw materials; calculating and weighing a required pure Mg ingot, mg-3wt.% Mn intermediate alloy and Mg-30wt.% Ce intermediate alloy; removing oxide skin and impurities on the surfaces of the pure Mg ingot and the intermediate alloy; the content of Mg in the pure Mg ingot is greater than 99.89wt.%;
Step two, preheating:
Preheating the raw materials weighed in the first step to 250 ℃; the preheating is carried out in a box-type resistance furnace;
Step three, smelting:
Putting the crucible into a well type resistance heating furnace, setting the temperature of the heating furnace to 760 ℃, introducing SF 6 and CO 2 mixed protective gas (the volume ratio of SF 6 to CO 2 is 1:40), when the temperature of the crucible reaches 650 ℃, putting the pure Mg ingot in the second step into the crucible for smelting, slagging off after the pure Mg ingot is completely melted, then sequentially adding preheated Mg-Mn intermediate alloy and Mg-Ce intermediate alloy, and fully preserving heat until the intermediate alloy is completely melted to obtain a magnesium alloy melt; stirring the magnesium alloy melt for 4min to fully and uniformly mix the alloy elements;
Removing scum on the surface of the magnesium alloy melt, and standing for 15min. Cooling the crucible in water under the protective atmosphere, taking out the crucible after the alloy melt in the crucible is completely cooled and solidified, and demolding to obtain a required alloy cast ingot;
Step four, preparing a magnesium alloy extrusion blank:
removing the oxidized part of the alloy ingot obtained in the third step, and obtaining a blank for extrusion with the diameter of 42mm and the height of 20mm by utilizing turning;
Step five, extrusion deformation:
Preheating the extrusion blank prepared in the fourth step to 340 ℃ and preserving heat for 15min, preheating an extrusion die to 340 ℃ before extrusion deformation treatment, setting the extrusion rate to be 0.1mm/s and the extrusion ratio to be 18:1, performing backward extrusion, and performing water quenching after extrusion deformation to obtain the Mg-1.4Mn-2.3Ce alloy.
In the embodiment, the light rare earth element Ce with lower cost is added on the basis of the Mg-Mn series alloy, the solid solubility of the light rare earth element Ce in magnesium is smaller, and the reduction degree of the heat conductivity of the magnesium alloy is small. The alloy element Mn is in a supersaturated state in the cast magnesium matrix, and Ce exists in the form of Mg 12 Ce phase and solute atoms. In the extrusion heat deformation process, the Mg 12 Ce phase can effectively pin the grain boundary and provide heterogeneous nuclear points to promote dynamic recrystallization, refine the crystal grains of the extruded alloy and be crushed and decomposed into fine particles in the hot extrusion process, so that the Ce element can play roles of fine crystal strengthening, second phase strengthening and the like, and the alloy of the embodiment has higher strength. In addition, because the solid solubility of Mn and Ce is very low, a large amount of nanoscale second phases are dynamically precipitated in the extrusion process, and grain boundary movement can be blocked, so that the growth of recrystallized grains is inhibited. The solute atoms in the magnesium matrix are consumed while the alloy is strengthened by a large amount of nano-scale dynamic precipitated phases, so that the content of the solute atoms in the magnesium matrix is greatly reduced, the degree of lattice distortion of the magnesium matrix is greatly reduced, the scattering effect on electrons and phonons in the heat conduction process is obviously weakened, and the heat conductivity of the alloy is further improved.
At 25 ℃, the thermal conductivity of the Mg-1.4Mn-2.3Ce extruded alloy obtained in the embodiment is 140.5W/(m.K), the yield strength is 387.0MPa, the tensile strength is 395.8MPa, and the elongation is 5.9%.
Fig. 1 is a metallographic photograph of an alloy ingot obtained in step three of example 1, from which it can be seen that the microstructure of the as-cast Mg-1.4Mn-2.3Ce alloy consists essentially of an α -Mg matrix and eutectic structures along grain boundaries, the eutectic structures being approximately in a continuous network-like distribution, the Mg 12 Ce phase at dendrite spacing being in a lamellar structure of eutectic flakes, with a small amount of second phase particles also being present within the grains. Fig. 2 is a scanning electron microscope photograph of the Mg-1.4Mn-2.3Ce alloy (extruded state) obtained in the step five of example 1, and it can be seen that the Mg 12 Ce phase in the extruded alloy is crushed into fine particles and distributed in a streamline shape along the extrusion direction, so as to play a role in reinforcing the second phase and improve the strength of the alloy. In addition, a large amount of nano precipitated phase alpha-Mn exists, so that the alloy maintains high heat conductivity and also has important contribution to strength.
Example 2
The present embodiment differs from embodiment 1 in that: the specific extrusion deformation process is different, and the extrusion deformation process in this embodiment is as follows: preheating the extrusion blank prepared in the fourth step to 310 ℃, preserving heat for 15min, preheating an extrusion die to 310 ℃ before extrusion deformation treatment, setting the extrusion rate to be 0.05mm/s, and setting the extrusion ratio to be 18: and 1, performing backward extrusion, and performing water quenching after extrusion deformation. The remainder was the same as in example 1.
The extruded alloy prepared in this example has the following comprehensive properties: the thermal conductivity is 134.5W/(m.K), the yield strength is 415.8MPa, the tensile strength is 429.4MPa, and the elongation is 7.5%.
Example 3
The present embodiment differs from embodiment 1 in that: the alloy composition and the extrusion deformation specific process are different. The alloy in the embodiment comprises the following elements in percentage by mass: mn:0.8wt.%, ce:1.8wt.% of unavoidable impurities such as Mg, fe, si, and the like, in balance. The extrusion deformation process is as follows: preheating the extrusion blank prepared in the step four in the example 1 to 300 ℃ and preserving heat for 15min, preheating an extrusion die to 300 ℃ before extrusion deformation treatment, setting the extrusion rate to 0.1mm/s, and setting the extrusion ratio to 22: and 1, performing backward extrusion, and performing water quenching after extrusion deformation. The remainder was the same as in example 1.
The extruded alloy prepared in this example has the following comprehensive properties: the thermal conductivity is 141W/(m.K), the yield strength is 372.7MPa, the tensile strength is 385.8MPa, and the elongation is 7.4%.
Example 4
The present embodiment differs from embodiment 3 in that: the mass percentages of elements in the prepared alloy are as follows: mn:1.1wt.%, ce:2.1wt.% and the balance of Mg and unavoidable impurities such as Fe, si, etc. The remainder was the same as in example 3.
The extruded alloy prepared in this example has the following comprehensive properties: the thermal conductivity is 139.5W/(m.K), the yield strength is 385.7MPa, the tensile strength is 395.3MPa, and the elongation is 7.1%.
Example 5
The present embodiment differs from embodiment 1 in that: the mass percentages of elements in the prepared alloy are as follows: mn:1.6wt.%, la:2.6wt.% and the balance of Mg and unavoidable impurities such as Fe, si, etc. The remainder was the same as in example 1.
The extruded alloy prepared in this example has the following comprehensive properties: the thermal conductivity is 138.7W/(m.K), the yield strength is 363.1MPa, the tensile strength is 378.5MPa, and the elongation is 8.1%.
Example 6
The present embodiment differs from embodiment 1 in that: the mass percentages of elements in the prepared alloy are as follows: mn:1.6wt.%, la:1.0wt.%, ce:1.5wt.% of unavoidable impurities such as Mg, fe, si, and the like, with the balance being. The remainder was the same as in example 1.
The extruded alloy prepared in this example has the following comprehensive properties: the thermal conductivity is 139.6W/(m.K), the yield strength is 388.5MPa, the tensile strength is 398.6MPa, and the elongation is 5.3%.
Comparative example 1
This comparative example differs from example 1 in that: the mass percentages of elements in the prepared alloy are as follows: mn:1.5wt.% of unavoidable impurities such as Mg, fe, si, and the like, with the balance being. The remainder was the same as in example 1.
The extruded alloy prepared in this comparative example has the following comprehensive properties: the thermal conductivity is 143.0W/(m.K), the yield strength is 185.2MPa, the tensile strength is 220.2MPa, and the elongation is 21.7%. The thermal conductivity and elongation of comparative example 1, although higher than those of example 1, were much lower in tensile strength than example 1, mainly due to the high recrystallization ratio and slightly coarse grains in the alloy of comparative example 1. Furthermore, the absence of Mg-RE phase in the alloy of comparative example 1 further results in lower strength.
Comparative example 2
This comparative example differs from example 1 in that: the mass percentages of elements in the prepared alloy are as follows: mn:1.5wt.%, nd:2.5wt.% of unavoidable impurities such as Mg and Fe, si, etc. in balance.
The extruded alloy prepared in this comparative example has the following comprehensive properties: the thermal conductivity was 124.9W/(mK), the yield strength was 385.2MPa, and the tensile strength was 393.1MPa. The tensile strength of comparative example 2 is comparable to that of example 1, but the thermal conductivity is reduced by 11% compared to example 1. The thermal conductivity of the comparative example is relatively low, mainly due to the fact that the maximum solid solubility of rare earth element Nd in Mg (3.6 wt.%) in the alloy of comparative example 2 is greater than that of rare earth element Ce (1.7 wt.%) so that the degree of lattice distortion of the matrix is greater.
Comparative example 3
This comparative example differs from example 1 in that: the mass percentages of elements in the prepared alloy are as follows: mn:1.5wt.%, gd:2.5wt.% of unavoidable impurities such as Mg and Fe, si, etc. in balance.
The extruded alloy prepared in this comparative example has the following comprehensive properties: the thermal conductivity was 86.4W/(mK), the yield strength was 349.3MPa, and the tensile strength was 358MPa. The thermal conductivity of comparative example 3 was significantly reduced compared to example 1, by about 38.5% lower than example 1. Mainly due to the fact that the maximum solid solubility of the heavy rare earth element Gd added in the alloy of comparative example 3 in Mg is very high, which can reach 23.5wt.%, thus causing serious lattice distortion of the matrix, thereby greatly reducing the thermal conductivity of the alloy. Further, in this comparative example, the grain refining effect and the second phase strengthening effect of Gd element on the alloy are weak, and thus the tensile strength thereof is also lower than that of example 1.
The above embodiments are only illustrative of the preferred embodiments of the present invention and are not intended to limit the scope of the present invention, and various modifications and improvements made by those skilled in the art to the technical solutions of the present invention should fall within the protection scope defined by the claims of the present invention without departing from the design spirit of the present invention.
Claims (8)
1. The high-heat-conductivity high-strength wrought magnesium alloy is characterized in that the high-heat-conductivity high-strength wrought magnesium alloy is an Mg-Mn-X alloy system; wherein X is a light rare earth element, the content is 0.5-5.0 wt.%, and the content of Mn is 1.4-4.0 wt.%; the balance of Mg and unavoidable impurities;
the light rare earth element is one or two of La and Ce;
The high-heat-conductivity high-strength deformed magnesium alloy has tensile yield strength of 363-416 MPa, tensile strength of 379-430 MPa, elongation of 5-10% and room temperature thermal conductivity of 135-141W/(m.K).
2. The method for preparing the high-heat-conductivity high-strength wrought magnesium alloy according to claim 1, which is characterized by comprising the following steps:
(1) Preparing raw materials according to the element proportion;
(2) Preheating the raw materials, smelting in a protective atmosphere, and cooling to obtain an alloy ingot;
(3) Preparing the alloy ingot into a blank for extrusion, extruding and deforming the blank for extrusion, and carrying out cold quenching to obtain the high-heat-conductivity high-strength deformed magnesium alloy.
3. The method according to claim 2, wherein the preheating in step (2) is performed at a temperature of 200 to 300 ℃.
4. The method according to claim 2, wherein the gas in the protective atmosphere in the step (2) is a mixed gas of SF 6 and CO 2.
5. The method of claim 2, wherein the starting materials in step (1) are pure Mg ingots, mg-Mn master alloys and Mg-light rare earth master alloys.
6. The method according to claim 5, wherein the smelting in step (2) is performed by: firstly, melting a pure Mg ingot, then adding an Mg-Mn intermediate alloy and an Mg-light rare earth element intermediate alloy, standing, preserving heat, and stirring to finish smelting; the melting temperature of the pure Mg ingot is 720-760 ℃; the standing and heat preserving time is 10-20 min; the stirring time is 3-5 min.
7. The method according to claim 2, wherein the extrusion deformation in step (3) is preceded by a preheating step; the preheating temperature is 300-400 ℃ and the preheating time is 10-30 min.
8. The preparation method according to claim 2, wherein the extrusion ratio of the extrusion deformation in the step (3) is (10-25): 1, and the extrusion rate is 0.05-5 mm/s.
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| CN109628814A (en) * | 2019-02-22 | 2019-04-16 | 中国科学院长春应用化学研究所 | Weight rare earth complex intensifying heat resistance magnesium alloy and preparation method thereof |
| CN113293329A (en) * | 2020-02-21 | 2021-08-24 | 宝山钢铁股份有限公司 | Low-cost high-strength high-heat-conductivity magnesium alloy material and manufacturing method thereof |
| CN113322404A (en) * | 2021-06-03 | 2021-08-31 | 哈尔滨工业大学 | High-thermal-conductivity high-strength Mg-Al-La-Mn wrought magnesium alloy and preparation method thereof |
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