High-plasticity double-isomerism ceramic particle reinforced magnesium-based composite material and preparation method thereof

Abstract

The invention discloses a high-plasticity double-isomerism ceramic particle reinforced magnesium-based composite material and a preparation method thereof.The preparation method is characterized by comprising the following steps that S1, nano titanium carbide particles, AZ61 magnesium alloy spherical powder and stearic acid are prepared; s2, all the raw materials in the step S1 are mixed and subjected to ball milling, and flaky composite powder is obtained; s3, the AZ61 magnesium alloy spherical powder and the flaky composite powder are mixed, then powder loading and cold pressing are carried out, and a powder pressing block is obtained; and S4, the powder briquettes are subjected to sintering, hot pressing and cooling and then subjected to hot extrusion deformation, and the double-isomerism magnesium-based composite material is obtained. According to the preparation method, the double-isomerism (namely the grain size of a double-peak structure and the micro-nano particles in non-uniform distribution) magnesium-based composite material can be obtained, and the plasticity of the magnesium-based composite material can be remarkably improved, so that the ceramic particle reinforced magnesium-based composite material has higher strength and plasticity.

Description

Technical Field

[0001] The present invention relates to the technical field of metal matrix composites, and particularly relates to a highly plastic dual - heterogeneous ceramic particle - reinforced magnesium matrix composite and a preparation method thereof. Background Art

[0002] Under the background that modern industry has increasingly stringent requirements for material properties, lightweight has become a key development trend. Ceramic particle - reinforced magnesium matrix composites have shown great application potential in the fields of aerospace, automotive, etc. due to their advantages such as low density, high specific strength, high elastic modulus, good creep resistance and wear resistance. However, this type of material has the prominent problem of low plasticity, which severely restricts its large - scale application.

[0003] The preparation of ceramic particle - reinforced magnesium matrix composites is mostly based on the idea of uniform dispersion to prepare composites with uniform microstructures. Although the prior art has improved the strength of composites by forming heterogeneous structures, their plasticity is still poor, and it is difficult to achieve fine regulation of the heterogeneous structures. Summary of the Invention

[0004] In view of the above problems, the present invention aims to provide a highly plastic dual - heterogeneous ceramic particle - reinforced magnesium matrix composite and a preparation method thereof.

[0005] The technical solution of the present invention is as follows:

[0006] On the one hand, a preparation method of a highly plastic dual - heterogeneous ceramic particle - reinforced magnesium matrix composite is provided, including the following steps:

[0007] S1: Prepare nano - titanium carbide particles, AZ61 magnesium alloy spherical powder and stearic acid;

[0008] S2: Mix and ball - mill the raw materials in step S1 to obtain flaky composite powder;

[0009] S3: Mix the AZ61 magnesium alloy spherical powder and the flaky composite powder, then load the powder and perform cold pressing to obtain a powder compact;

[0010] S4: Sinter and hot - press the powder compact, and perform hot extrusion deformation after cooling to obtain a dual - heterogeneous magnesium matrix composite.

[0011] Preferably, in step S1, the particle size of the AZ61 magnesium alloy spherical powder is 50 - 100 μm; in step S2, the layer thickness of the flaky composite powder is 3 - 20 μm.

[0012] Preferably, in step S2, the mass of the nano titanium carbide particles accounts for 1-4 wt.% of the flaky composite powder, and the mass of the stearic acid accounts for 0.5-1.5 wt.% of the flaky composite powder; in step S3, the mass of the AZ61 magnesium alloy spherical powder accounts for 10-75 wt.% of the total powder in step S3.

[0013] Preferably, in step S2, when ball milling, the grinding media are stainless steel balls, the ball-to-material ratio is 15:1-20:1, the filling coefficient of the grinding media and the material to be ball milled relative to the ball mill tank is 0.3-0.4. Then, first perform low-speed ball milling at a rotational speed of 120-180 rpm for 18-30 h, and then perform high-speed ball milling at a rotational speed of 300-350 rpm for 0.5-1 h; during the ball milling process, pause for 5 min every 30 min of low-speed ball milling, take out the ball mill tank and shake it by hand, and fill with an inert gas every 2 h; pause for 5 min every 15 min of high-speed ball milling, and take out the ball mill tank and shake it by hand.

[0014] Preferably, in step S3, when mixing, use agate balls for ball milling and mixing, the ball-to-material ratio is 5:1-1:1, the ball milling rotational speed is 80-150 rpm, and the ball milling time is 1-2 h.

[0015] Preferably, in step S3, when cold pressing, perform cold pressing on a vertical hydraulic press at a downward pressing speed of 0.5-1.5 mm / s. After the applied pressure reaches 1400-1700 KN, hold for 10-18 min.

[0016] Preferably, in step S4, when sintering, sinter at 490-520 °C for 1.5-2.5 h under an inert atmosphere condition.

[0017] Preferably, in step S4, when hot pressing, apply a uniaxial pressure to the sintered blank, perform hot pressing at a downward pressing speed of 0.5-1.5 mm / s. After the applied pressure reaches 1400-2000 KN, hold the pressure for 15-20 min.

[0018] Preferably, in step S4, when hot extrusion deformation is carried out, the extrusion temperature is 320-380 °C, the extrusion ratio is 15:1-25:1, and the extrusion speed is 0.5-1 mm / s.

[0019] On the other hand, a highly plastic dual-isomorphic ceramic particle-reinforced magnesium matrix composite is also provided, which is prepared by using the preparation method of the highly plastic dual-isomorphic ceramic particle-reinforced magnesium matrix composite described in any one of the above.

[0020] The beneficial effects of the present invention are:

[0021] (1) Compared with the ceramic particle-reinforced magnesium matrix composites prepared by the existing technology with a uniform dispersion idea, the present invention can significantly improve the plasticity of the ceramic particle-reinforced magnesium matrix composites by introducing a heterogeneous structure.

[0022] (2) Based on the bimodal grain structure, the present invention introduces a large number of Mg 17 Al 12 second phases. Compared with the magnesium matrix composites with a bimodal grain structure having only a single heterogeneous level, the magnesium matrix composites with a dual heterogeneous structure (including not only the bimodal grain structure but also a non-uniform particle distribution) exhibit a more excellent plasticizing effect, which can enable the ceramic particle-reinforced magnesium matrix composites to undergo a greater degree of plastic deformation, effectively solving the problems of difficult processing and deformation of the ceramic particle-reinforced magnesium matrix composites.

[0023] (3) Compared with the heterogeneous structure magnesium matrix composites prepared by the melting method, the present invention adopts a powder metallurgy combined with a hot extrusion process to achieve fine control of the heterogeneous structure of the ceramic particle-reinforced magnesium matrix composites, such as the fraction of the coarse grain region, the fraction of the second phase in the coarse grain region, and the grain size of the coarse grain region.

[0024] (4) The preparation method of the present invention is applicable to the preparation of large bulk samples of ceramic particle-reinforced magnesium matrix composites, and has broad application prospects in industrial production. BRIEF DESCRIPTION OF THE DRAWINGS

[0025] In order to more clearly illustrate the technical solutions in the embodiments of the present invention or the prior art, the following will briefly introduce the drawings required for the description of the embodiments or the prior art. Obviously, the following drawings are only some embodiments of the present invention. For those of ordinary skill in the art, without creative efforts, other drawings can also be obtained based on these drawings.

[0026] Figure 1 FIGURES showing the metallographic and SEM images of the magnesium matrix composites of Example 1 and Comparative Example 2; where (a) and (b) are the metallographic images of Example 1, (c) is the SEM image of Example 1, (d) and (e) are the metallographic images of Comparative Example 2, and (f) is the SEM image of Comparative Example 2;

[0027] Figure 2 EDS surface scan images corresponding to different elements of the magnesium matrix composites of Example 1;

[0028] Figure 3 Metallographic image of the magnesium matrix composites of Comparative Example 1;

[0029] Figure 4 FIGURES showing the metallographic images of the magnesium matrix composites of Example 2 and Comparative Example 3; where (a) is the metallographic image of Example 2 and (b) is the metallographic image of Comparative Example 3;

[0030] Figure 5 Tensile mechanical property curves of the magnesium matrix composites of Example 1, Comparative Example 1 and Comparative Example 2;

[0031] Figure 6 Tensile mechanical property curves of the magnesium matrix composites of Example 2, Comparative Example 1 and Comparative Example 3. Detailed implementation manners

[0032] The present invention will be further described below in conjunction with the accompanying drawings and embodiments. It should be noted that, without conflict, the embodiments in the present application and the technical features in the embodiments may be combined with each other. It should be pointed out that unless otherwise specified, all the technical and scientific terms used in the present application have the same meaning as commonly understood by those of ordinary skill in the technical field to which the present application belongs. The terms such as "including" or "comprising" used in the disclosure of the present invention mean that the elements or objects appearing before this word cover the elements or objects listed after this word and their equivalents, without excluding other elements or objects.

[0033] On the one hand, the present invention provides a preparation method of a high-plasticity double-isomorphic ceramic particle-reinforced magnesium matrix composite, comprising the following steps:

[0034] S1: Prepare nano titanium carbide particles, AZ61 magnesium alloy spherical powder and stearic acid;

[0035] S2: Mix and ball-mill the raw materials in step S1 to obtain flaky composite powder;

[0036] S3: Mix the AZ61 magnesium alloy spherical powder with the flaky composite powder, then load the powder and perform cold pressing to obtain a powder compact;

[0037] S4: Sinter and hot-press the powder compact, and perform hot extrusion deformation after cooling to obtain a double-isomorphic magnesium matrix composite.

[0038] In the present invention, first mix and ball-mill the nano titanium carbide particles and the AZ61 magnesium alloy spherical powder to obtain refined flaky composite powder; then mix the flaky composite powder with the unrefined AZ61 magnesium alloy spherical powder so that the final powder material includes powders of different scales, and then prepare a double-isomorphic magnesium matrix composite through cold pressing, sintering, cooling and hot extrusion deformation. The double isomorphism includes two aspects of isomorphism, namely the grain size of the bimodal structure and the non-uniformly distributed micro-nano particles (micron-scale Mg 17 Al 12 phase and nano TiC particles). Compared with the single-level isomorphic bimodal grain structure, the double isomorphism can significantly improve the plasticity of the magnesium matrix composite, thereby achieving the combination of higher strength and plasticity of the ceramic particle-reinforced magnesium matrix composite.

[0039] It should be noted that the AZ61 magnesium alloy spherical powder is used in the present invention because it can be ground into flakes and a second phase is formed subsequently. Other magnesium alloy spherical powders with such characteristics and functions in the prior art can also be applicable to the present invention.

[0040] In a specific embodiment, in step S1, the particle size of the AZ61 magnesium alloy spherical powder is 50 - 100 μm; in step S2, the layer thickness of the flaky composite powder is 3 - 20 μm. In this embodiment, by using flaky composite powders and magnesium alloy spherical powders with different scales, the powders after mixing in step S3 can still have different scales, so that the present invention can prepare a dual - isomeric magnesium - based composite material in combination with subsequent processes.

[0041] In a specific embodiment, in step S2, the mass of the nano - titanium carbide particles accounts for 1 - 4 wt.% of the flaky composite powder, and the mass of the stearic acid accounts for 0.5 - 1.5 wt.% of the flaky composite powder; in step S3, the mass of the AZ61 magnesium alloy spherical powder accounts for 10 - 75 wt.% of the total powder in step S3.

[0042] In a specific embodiment, in step S2, when ball - milling, the grinding media are stainless steel balls, the ball - to - powder ratio is 15:1 - 20:1, the filling coefficient of the ball - milling media and the material to be ball - milled relative to the ball - milling tank is 0.3 - 0.4. Then, it is first ball - milled at a low speed of 120 - 180 rpm for 18 - 30 h, and then ball - milled at a high speed of 300 - 350 rpm for 0.5 - 1 h; during the ball - milling process, it pauses for 5 min every 30 min of low - speed ball - milling, and the ball - milling tank is taken out and shaken by hand. Every 2 h, an inert gas is filled once; during high - speed ball - milling, it pauses for 5 min every 15 min, and the ball - milling tank is taken out and shaken by hand.

[0043] It should be noted that in the above - mentioned embodiment, the time of pausing and hand - shaking is not included in the total ball - milling time.

[0044] In a specific embodiment, in step S3, when mixing, agate balls are used for ball - milling and mixing, and the ball - to - powder ratio is 5:1 - 1:1, the ball - milling speed is 80 - 150 rpm, and the ball - milling time is 1 - 2 h; when cold - pressing, it is cold - pressed on a vertical hydraulic press at a pressing speed of 0.5 - 1.5 mm / s. After the applied pressure reaches 1400 - 1700 KN, it is maintained for 10 - 18 min.

[0045] In the above embodiments, using agate balls can reduce the impact and collision of grinding balls on the powder, ensuring that the coarse powder (i.e., the AZ61 magnesium alloy spherical powder) does not deform. Slowly pressing down at a pressing speed of 0.5 - 1.5 mm / s is beneficial to expel the gas in the powder and reduce the gap between powders.

[0046] In a specific embodiment, in step S4, during sintering, under an inert atmosphere condition, sinter at 490 - 520 °C for 1.5 - 2.5 h. Since the self-diffusion coefficient of magnesium alloy is low at 450 °C and the diffusion rate is very slow, it is likely to result in a low densification degree. In this embodiment, increasing the sintering temperature is beneficial to enhancing the diffusion ability of atoms. When using AZ61 magnesium alloy spherical powder, according to the phase diagram, when the sintering temperature of AZ61 alloy exceeds 530 °C, it belongs to the liquid-phase sintering range. To avoid the problem of excessive grain growth caused by entering the liquid-phase sintering range, the maximum temperature in this embodiment is limited to 520 °C. Generally speaking, when performing sintering in step S4 of the present invention, sintering can be carried out at a relatively high solid-phase sintering temperature of the magnesium alloy spherical powder.

[0047] In a specific embodiment, during sintering, first raise the temperature of the heating furnace to 400 °C and hold for 30 - 60 min. This step is to expel the gas in the furnace. Then raise the furnace temperature to 480 °C and hold for 10 min. After that, gradually raise the temperature to 520 °C, and for every 10 °C increase in temperature, hold for 5 min. The purpose of gradually raising the temperature is to avoid temperature overshoot, which may lead to exceeding the target sintering temperature and generating liquid phase. When the temperature is raised to 520 °C, hold for 30 - 60 min. The entire sintering process is carried out under the protection of an inert gas atmosphere, which can avoid oxidation during sintering.

[0048] In a specific embodiment, in step S4, during hot pressing, apply a uniaxial pressure to the sintered blank, and perform hot pressing at a pressing speed of 0.5 - 1.5 mm / s. After the applied pressure reaches 1400 - 2000 KN, hold the pressure for 15 - 20 min. In this embodiment, using the hot pressing process with these parameters is beneficial to reducing the sintering time, further reducing pores, and obtaining a composite blank with extremely high density.

[0049] In a specific embodiment, in step S4, during hot extrusion deformation, the extrusion temperature is 320 - 380 °C, the extrusion ratio is 15:1 - 25:1, and the extrusion speed is 0.5 - 1 mm / s. In this embodiment, using the hot extrusion deformation with these parameters can further densify the composite material and realize the regulation of the microstructure, introducing a second phase with non-uniform distribution.

[0050] It should be noted that the specific embodiments of the above cold pressing, sintering, hot pressing, and hot extrusion deformation are only the preferred embodiments of the present invention. Mainly through this process, in the case of sheet composite powders with different sizes and morphologies and unrefined magnesium alloy spherical powders, a magnesium matrix composite material with a dual heterogeneous structure (i.e., a bimodal grain size structure and non-uniformly distributed micro-nano particles (Mg 17 Al 12 phase and nano-TiC particles)) can be formed. Cold pressing, sintering, hot pressing, and hot extrusion deformation processes that use other parameters but can also produce the magnesium matrix composite material with this dual heterogeneous structure are also applicable to the present invention.

[0051] On the other hand, the present invention also provides a high-plasticity dual-isomorphic ceramic particle-reinforced magnesium matrix composite material, which is prepared by using the preparation method of the high-plasticity dual-isomorphic ceramic particle-reinforced magnesium matrix composite material described in any one of the above.

[0052] Example 1

[0053] A high-plasticity dual-isomorphic ceramic particle-reinforced magnesium matrix composite material is prepared through the following steps:

[0054] (1) Put nano-titanium carbide particles (accounting for 2 wt.% of the mixture in this step), AZ61 magnesium alloy spherical powders (particle size of 50 - 100 μm), and stearic acid (accounting for 1 wt.% of the mixture in this step) into a vacuum glove box. Use stainless steel ball mills to perform low-speed ball milling on the AZ61 magnesium alloy spherical powders and nano-titanium carbide particles at a ball-to-material ratio of 15:1 - 20:1 and a filling coefficient of the ball mills and the materials to be ball milled relative to the ball milling tank of 0.3 - 0.4 for 20 h at a rotation speed of 150 rpm, and then perform high-speed ball milling at a rotation speed of 300 rpm for 1 h. During the ball milling process, the low-speed ball milling pauses for 5 min every 30 min, and the ball milling tank is taken out and shaken by hand, and argon is filled once every 2 h; during the high-speed ball milling process, it pauses for 5 min every 15 min, and the ball milling tank is taken out and shaken by hand. Finally, ball milled and refined TiC / AZ61 sheet composite powders (sheet layer thickness of 2 - 8 μm) are obtained;

[0055] (2) After the TiC / AZ61 sheet composite powders are cooled, replace the stainless steel ball mills with agate balls in the vacuum glove box, and then add unball milled AZ61 magnesium alloy spherical powders (accounting for 50 wt.% of the mixture in this step) into the ball milling tank, and perform ball milling to mix evenly. The ball-to-material ratio is 1:1, the ball milling rotation speed is 120 rpm, and the ball milling time is 1.5 h. Wait for the powders to cool and then load the powders, and then place them together with the mold on a 200T hydraulic press for cold pressing. After pressing to the maximum pressure of 1700 KN, hold for 12 min to obtain a powder compact.

[0056] (3)Put the powder compact together with the mold into a sintering furnace. First, raise the temperature of the heating furnace to 480 °C (to prevent temperature overshoot) and hold for 10 min, then gradually raise the temperature to 520 °C, holding for 5 min every 10 °C increase. After reaching 520 °C, hold for 30 - 60 min. The entire sintering process is carried out under the protection of an argon atmosphere. After sintering is completed, take out the mold and the blank together, and then perform hot pressing on a 200T hydraulic press at a downward pressing speed of 0.75 mm / s. After pressing to the maximum pressure of 1500 KN, hold the pressure for 15 min. After hot pressing is completed, demold. After demolding, perform hot extrusion deformation on the blank at a temperature of 350 °C, an extrusion ratio of 20:1, and an extrusion speed of 0.75 mm / s, finally obtaining a dual heterogeneous structure magnesium matrix composite containing 50% coarse grain zone and 1 wt.% nano-TiC particles.

[0057] Example 2

[0058] Different from Example 1, in step (1) of this example, the dosage of nano-titanium carbide particles is 4 wt.%, in step (2), the dosage of un-milled AZ61 magnesium alloy spherical powder is 75 wt.%, and in step (3), a dual heterogeneous structure magnesium matrix composite containing 75% coarse grain zone and 1.3 wt.% nano-TiC particles is obtained.

[0059] Comparative Example 1

[0060] Different from Example 1, in step (1) of this comparative example, the dosage of nano-titanium carbide particles is 1 wt.%, and in step (2), un-milled AZ61 magnesium alloy spherical powder is not added.

[0061] Comparative Example 2

[0062] Different from Example 1, in step (1) of this comparative example, the dosage of nano-titanium carbide particles is 1 wt.%, only low-speed ball milling at a rotation speed of 150 rpm for 12 h is carried out during ball milling, in step (2), un-milled AZ61 magnesium alloy spherical powder is not added, and in step (3), the extrusion speed of hot extrusion deformation is 3.5 mm / s.

[0063] Comparative Example 3

[0064] Different from Example 2, in step (1) of this comparative example, the dosage of nano-titanium carbide particles is 1 wt.%, only low-speed ball milling at a rotation speed of 150 rpm for 20 h is carried out during ball milling, in step (2), un-milled AZ61 magnesium alloy spherical powder is not added, and in step (3), the extrusion speed of hot extrusion deformation is 3.5 mm / s.

[0065] Test Example 1

[0066] Observe the microstructures of each example and each comparative example. The metallographic and SEM images of Example 1 and Comparative Example 2 are as Figure 1 As shown, the EDS surface scan images corresponding to different elements in Example 1 are as Figure 2 shown, and the metallographic image of Comparative Example 1 is as Figure 3 shown, and the metallographic images and SEM images of Example 2 and Comparative Example 3 are as Figure 4 shown.

[0067] From Figure 1 it can be seen that the magnesium-based composite material of Example 1 of the present invention not only has a bimodal grain structure, but also contains a large amount of Mg 17 Al 12 second phase; while the magnesium-based composite material prepared in Comparative Example 2 also has a bimodal grain structure with a 50% coarse grain region, but there are no second-phase particles in its coarse grain region. From Figure 2 it can be seen that Al element and Ti element show banded enrichment, proving that the nano-TiC particles and micron-sized Mg 17 Al 12 are unevenly distributed. In fact, combined with Figure 1 (c), it can be seen that there are a large number of fine Mg 17 Al 12 second phases in the middle of the band enriched with Al element. Since their distribution is uniform and their size is fine, in the sub-micron range. Therefore Figure 2 the enrichment of Al element is not shown in the band enriched with Al element in

[0068] From Figure 3 it can be seen that in the magnesium-based composite material with the same content of nano titanium carbide particles, the magnesium-based composite material prepared without adding unmilled AZ61 magnesium alloy spherical powder shows uniform microstructural characteristics.

[0069] From Figure 4 it can be seen that the magnesium-based composite material of Example 2 of the present invention is similar to that of Example 1, and also has both a bimodal grain structure and contains a large amount of Mg 17 Al 12 second phase; while the magnesium-based composite material prepared in Comparative Example 3 also has a bimodal grain structure with a 75% coarse grain region, but there are no second-phase particles in its coarse grain region.

[0070] Test Example 2

[0071] The tensile mechanical properties of each example and each comparative example were tested, and the results are as Figure 5 and Figure 6 shown. From Figure 5It can be seen that the dual - heterogeneous magnesium - based composite material prepared in Example 1 of the present invention obtains the best comprehensive mechanical properties (tensile strength of about 403 MPa, yield strength of about 320 MPa, elongation of about 9.7%). Compared with the homogeneous - structure magnesium - based composite material prepared in Comparative Example 1, the elongation is increased by 73%. Compared with the homogeneous - structure magnesium - based composite material prepared in Comparative Example 1, the elongation of the bimodal - grain - structure magnesium - based composite material prepared in Comparative Example 2 is increased by 50%. However, under the condition of the same coarse - grain - zone fraction (50%), the dual - heterogeneous magnesium - based composite material of the present invention has a better elongation effect. Compared with the material only having a bimodal - grain structure, the dual - heterogeneous magnesium - based composite material of the present invention has a better plasticizing effect.

[0072] From Figure 6 It can be seen that the dual - heterogeneous magnesium - based composite material prepared in Example 2 of the present invention obtains the best comprehensive mechanical properties (tensile strength of about 393 MPa, yield strength of about 289 MPa, elongation of about 14.5%). Compared with the homogeneous - structure magnesium - based composite material prepared in Comparative Example 1, the elongation of Example 2 is significantly increased, up to 159%. However, compared with the homogeneous - structure magnesium - based composite material prepared in Comparative Example 1, the elongation of the bimodal - grain - structure magnesium - based composite material prepared in Comparative Example 2 is increased by 68%. Under the condition of the same coarse - grain - zone fraction (75%), the dual - heterogeneous magnesium - based composite material of the present invention has a better elongation effect. The dual - heterogeneous magnesium - based composite material of the present invention has a more excellent plasticizing effect compared with the bimodal - grain structure.

[0073] It should be noted that the above - mentioned examples and their test results are only part of the examples and their test results of the present invention. The products prepared by using the preparation method of the present invention by changing the agent content, ball - milling parameters, cold - pressing parameters, sintering parameters, hot - pressing parameters, hot - extrusion deformation parameters, etc. all have similar properties, have good plasticity and strength, and can achieve both high strength and high plasticity.

[0074] In summary, the present invention can improve the plasticity of the magnesium - based composite material while increasing the strength by using a dual - heterogeneous structure (i.e., the grain size of the bimodal structure and the non - uniformly distributed micro - and nano - particles). Compared with the prior art, there is a significant progress.

[0075] The above - mentioned are only representative embodiments of the present invention, and do not impose any form of limitation on the present invention. Any person skilled in the art, without departing from the technical solution of the present invention, makes some changes or modifications using the disclosed technical content, and such embodiments are equivalent embodiments of the present invention. However, as long as it does not depart from the technical content of the present invention, any simple modification, equivalent change, and modification made to the above - mentioned embodiments according to the technical essence of the present invention still fall within the scope of the technical solution of the present invention.

Claims

1. A preparation method of a high-plasticity dual-isomer ceramic particle-reinforced magnesium matrix composite, characterized in that, It includes the following steps: S1: Prepare titanium carbide nanoparticles, AZ61 magnesium alloy spherical powder, and stearic acid; S2: Mix and ball-mill the raw materials in step S1 to obtain flaky composite powder; S3: Mix the AZ61 magnesium alloy spherical powder with the flaky composite powder, then load the powder and perform cold pressing to obtain a powder compact; S4: Sinter and hot press the powder compact, and perform hot extrusion deformation after cooling to obtain a dual-textured magnesium matrix composite.

2. The preparation method of the highly plastic dual-isomeric ceramic particle-reinforced magnesium matrix composite according to claim 1, characterized in that, In step S1, the particle size of the AZ61 magnesium alloy spherical powder is 50 - 100 μm; in step S2, the layer thickness of the flaky composite powder is 3 - 20 μm.

3. The preparation method of the highly plastic dual-isomeric ceramic particle-reinforced magnesium matrix composite according to claim 1, characterized in that In step S2, the mass of the titanium carbide nanoparticles accounts for 1 - 4 wt.% of the flaky composite powder, and the mass of the stearic acid accounts for 0.5 - 1.5 wt.% of the flaky composite powder; in step S3, the mass of the AZ61 magnesium alloy spherical powder accounts for 10 - 75 wt.% of the total powder in step S3.

4. The preparation method of the highly plastic dual-isomer ceramic particle-reinforced magnesium matrix composite according to claim 1, characterized in that, In step S2, when performing ball milling, the grinding media are stainless steel balls, the ball-to-powder ratio is 15:1 - 20:1, the filling coefficient of the grinding media and the material to be ball milled relative to the ball mill tank is 0.3 - 0.

4. Then, first perform low-speed ball milling at a rotation speed of 120 - 180 rpm for 18 - 30 h, and then perform high-speed ball milling at a rotation speed of 300 - 350 rpm for 0.5 - 1 h; during the ball milling process, pause for 5 min every 30 min of low-speed ball milling and take out the ball mill tank to shake by hand, and fill with an inert gas every 2 h; pause for 5 min every 15 min of high-speed ball milling and take out the ball mill tank to shake by hand.

5. The preparation method of the highly plastic dual-isomer ceramic particle-reinforced magnesium matrix composite according to claim 1, characterized in that, In step S3, when performing mixing, use agate balls for ball milling and mixing, the ball-to-powder ratio is 5:1 - 1:1, the ball milling rotation speed is 80 - 150 rpm, and the ball milling time is 1 - 2 h.

6. The preparation method of the high-plasticity dual-isomer ceramic particle-reinforced magnesium matrix composite according to claim 1, characterized in that, In step S3, when performing cold pressing, perform cold pressing on a vertical hydraulic press at a downward pressing speed of 0.5 - 1.5 mm / s. After the applied pressure reaches 1400 - 1700 KN, hold for 10 - 18 min.

7. The preparation method of the high-plasticity dual-isomer ceramic particle-reinforced magnesium matrix composite according to claim 1, characterized in that In step S4, when performing sintering, sinter at 490 - 520 °C for 1.5 - 2.5 h under an inert atmosphere condition.

8. The preparation method of the highly plastic double-isomer ceramic particle-reinforced magnesium matrix composite material according to claim 1, characterized in that, In step S4, when performing hot pressing, apply a uniaxial pressure to the sintered blank, perform hot pressing at a downward pressing speed of 0.5 - 1.5 mm / s. After the applied pressure reaches 1400 - 2000 KN, hold the pressure for 15 - 20 min.

9. The preparation method of the highly plastic dual-isomeric ceramic particle-reinforced magnesium matrix composite according to claim 1, wherein, In step S4, when performing hot extrusion deformation, the extrusion temperature is 320 - 380 °C, the extrusion ratio is 15:1 - 25:1, and the extrusion speed is 0.5 - 1 mm / s.

10. A high-plasticity dual-isomeric ceramic particle-reinforced magnesium matrix composite material, characterized in that, It is prepared by using the preparation method of the highly plastic dual-textured ceramic particle-reinforced magnesium matrix composite according to any one of claims 1 - 9.

Images