CN113234952A - Brick-like bionic composite preparation of ceramic reinforced aluminum-based composite material - Google Patents

Brick-like bionic composite preparation of ceramic reinforced aluminum-based composite material Download PDF

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CN113234952A
CN113234952A CN202110505604.1A CN202110505604A CN113234952A CN 113234952 A CN113234952 A CN 113234952A CN 202110505604 A CN202110505604 A CN 202110505604A CN 113234952 A CN113234952 A CN 113234952A
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brick
composite material
aluminum
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CN113234952B (en
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范根莲
张志明
李志强
谭占秋
张荻
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Shanghai Jiaotong University
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • B22F1/0003—
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/06—Metallic powder characterised by the shape of the particles
    • B22F1/068—Flake-like particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0068—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only nitrides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
    • B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling

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Abstract

The invention provides a brick-like bionic composite preparation ceramic reinforced aluminum-based composite material, which is characterized in that micro-nano aluminum sheet elements with preferred orientation are prepared in advance and are uniformly mixed with sheet ceramic elements, the two sheet elements are alternately stacked in a brick-like mode under the dual actions of gravity and external force in the densification process, and the brick-like bionic ceramic reinforced aluminum-based composite material can be obtained through further processing deformation. Wherein, the thickness of the aluminum sheet and the ceramic sheet is only hundreds of nanometers, and the structure and the scale effectively imitate the structure of a pearl layer. The substrate of the bricklaying-like bionic composite material presents an ultrafine grain layered structure, and the flaky ceramic plates can also effectively block the expansion of cracks, so that the high-strength plastic matching is kept under the condition of fully exerting the dual mechanisms of ultrafine grain strengthening and crack deflection. The ceramic reinforced aluminum-based composite material prepared by the invention has the advantages of low cost, wide application range and higher comprehensive mechanical property.

Description

Brick-like bionic composite preparation of ceramic reinforced aluminum-based composite material
Technical Field
The invention relates to the field of metal matrix composite materials, in particular to a brick-like bionic composite preparation method of a ceramic reinforced aluminum matrix composite material.
Background
Many biomaterials in nature have been developed for a long time, and their structures and properties have reached nearly perfect levels, such as multi-layered board structure of bones, gradient layered structure of bamboo, and laminated structure of shell pearl layer. The nacreous layer of the shell is the hottest structural bionic object at present, and the nacreous layer is a self-assembled 'brick-mud' laminated structure which takes calcium carbonate (-95 vol.%) nano thin sheets (with the thickness of-500 nm) as 'bricks' and organic matter (-5 vol.%) and with the thickness of-30 nm) as 'mud', so that the overall strength of the shell is not sacrificed, the plastic toughness is greatly improved, and the comprehensive performance of the excellent strength and the plastic toughness is obtained. Therefore, the shell nacre layer becomes a research template for a plurality of researchers simulating and realizing material toughening at home and abroad, and the composite material is developed towards more excellent comprehensive performance. The concept is quickly verified and applied to various ceramic matrix composite materials and resin matrix composite materials, however, due to the lack of proper preparation technology of the metal matrix composite materials, even if the shell-like laminated structure optimization is urgently needed to realize the application in various practical situations due to the unmatched strength and plasticity and toughness, the development is still limited, and related research is also very limited.
Several methods for preparing shell-like pearl layer metal-based composite materials are also developed primarily at home and abroad, which mainly comprise the following steps: preparation of Al by Directional solidification of ceramic slurries by the "Freeze casting method" of the novel biological approach to the design of high-performance ceramic-metal composites, 7(2010)741-753, university of California, Ricthie group ("A novel biological approach to the design of high-performance ceramic-metal composites")2O3A layered skeleton, into which Al-Si is then impregnatedThe crystal alloy obtains Al containing interlayer inorganic bridging2O3A/Al-Si laminated composite material. However, nanocrystalline/ultrafine grained (e.g., mineral layer spacing of 500nm in mother-of-pearl) was observed from the internal structure of the shell as an important factor for strengthening and toughening the characteristics. The thickness of the layer in the composite material prepared by the freezing casting method is reduced to more than 10 microns at least, but is still dozens of times higher than the real thickness of the pearl layer, and the optimal toughness matching is not obtained.
The research on the preparation of the ceramic reinforced aluminum-based composite material by the brick-like bionic composite is not found in the existing literature and invention search.
In addition, Zhang et al, in the literature [ "bioinpred, graphene-enabled Ni composites with high strength and hardness" science advances,5(2019) eaav5577], obtained a nickel-based composite material with a "brick-ash" like structure by in-situ reaction and later thermal deformation, and its comprehensive mechanical properties were greatly improved. However, the process is complicated and long in period, and the content of the brick-shaped reinforcement obtained by the in-situ reaction has great uncertainty.
Through the search of the existing patent literature, CN201710570994 discloses a high-volume ceramic-metal layered composite material and a preparation method thereof, the preparation method related to the high-volume ceramic-metal layered composite material still belongs to the aforementioned freeze casting method, the layered thickness is still larger than 5 μm, although the high-volume ceramic-metal layered composite material structurally simulates the brick-ash structure of shells, but the scale of the shell pearl layer is not actually reached.
Disclosure of Invention
The invention aims to provide a brick-like bionic composite preparation ceramic reinforced aluminum-based composite material, wherein a ceramic reinforcement body and a substrate are alternately stacked by taking a structure similar to a brick as a basic element, so that a shell pearl layer structure is effectively simulated from the brick-ash-shaped structure and the scale (less than 500nm), and the comprehensive mechanical property of the ceramic reinforced aluminum-based composite material is obviously improved compared with that of the conventional ceramic reinforced aluminum-based composite material. The preparation method disclosed by the invention is time-saving and energy-saving, improves the comprehensive mechanical property of the composite material while reducing the preparation cost, and has huge large-scale application potential.
In order to achieve the purpose, micro-nano aluminum sheet elements with preferred orientation are prepared in advance through ball milling for a certain time, and are mixed with sheet ceramic elements to form a brick-like bionic structure ingot blank through densification and sintering, wherein the thicknesses of the aluminum sheets and the ceramic sheets are only hundreds of nanometers, the structure and the scale effectively imitate a pearl layer structure, and the brick-like bionic composite ceramic reinforced aluminum-based composite material can be obtained through further deformation processing. The substrate of the bricklaying-like bionic composite material has an ultrafine grain layered structure, so that dislocation motion in crystal grains is facilitated, and the flaky ceramic piece can also effectively block the expansion of cracks, so that high-strength plastic matching is kept under the condition of fully exerting the dual mechanisms of ultrafine grain strengthening and crack deflection.
Specifically, the method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite comprises the following steps:
(1) preparing micro-nano aluminum sheet elements: ball-milling spherical aluminum powder to obtain micro-nano flaky aluminum powder with preferred orientation;
(2) uniformly mixing the micro-nano aluminum sheet element and the flaky ceramic reinforcement element by adopting a roller powder mixing mode;
(3) carrying out densification treatment to obtain a brick-like bionic composite powder ingot blank;
(4) and sintering and thermally deforming the powder ingot blank to obtain the brick-like bionic composite ceramic reinforced aluminum-based composite material.
As an embodiment of the present invention, the ball milling adopts the following parameters: the mass ratio of the steel balls to the aluminum powder is 10: 1-30: 1, the rotating speed is 50-400 r/min, and the time is 2-10 h.
According to one embodiment of the invention, the thickness of the micro-nano aluminum sheet element is between 0.2 and 0.5 μm, and the sheet diameter is between 5 and 50 μm.
In one embodiment of the present invention, the ceramic reinforcement member element has a thickness of 0.2 to 0.5 μm and a diameter of 5 to 30 μm.
In the system, the micro-nano aluminum sheet elements and the flaky ceramic reinforcement elements with the diameter-thickness ratio of less than 500nm are used, so that the shape matching can be realized, and the micro-nano aluminum sheet elements and the flaky ceramic reinforcement elements can be basically arranged in parallel. Wherein the aspect ratio is a comparison of diameter and thickness. In the invention, the diameter-thickness ratio of the micro-nano aluminum sheet element to the sheet ceramic reinforcement element is over 10, and the interaction stacking is good. If the radius-thickness ratio is smaller, the interactive stacking is not realized, and the interactive stacking is randomly arranged.
In one embodiment of the invention, in the roller powder mixing mode, the mass ratio of the agate balls to the powder is 2: 1-20: 1, the rotating speed: 5-100 rpm. In step (2), in the roller mixing, the added shearing force of the agate balls can open the agglomerated powder, but the shearing force needs to be low enough not to damage the powder form; therefore, the mass ratio of the agate balls to the powder is 2: 1-20: 1, the rotating speed is as follows: 5-100 rpm. For other powder mixing methods, such as mixing two powders, stirring alone cannot disperse the two powders uniformly.
As an embodiment of the invention, the volume fraction of the sheet-like ceramic reinforcement in the composite material is 1-30 vol.%. In the system of the present invention, too high a volume fraction may cause significant agglomeration.
As an embodiment of the invention, the densification treatment adopts a cold pressing process, wherein the cold pressing temperature is 20-200 ℃, and the pressure is 300-500 MPa. In the system of the invention, the powder is first shaped by cold pressing; the mold can not bear the excessive pressure, and the density cannot be realized due to the excessive pressure; therefore, the pressure is 300-500 MPa. As an implementation example of the invention, the cold pressing temperature is further selected to be 100-200 ℃.
As an embodiment of the invention, the sintering process is vacuum hot pressing sintering, atmosphere sintering, spark ion beam sintering, hot isostatic pressing sintering; and the sintering temperature is 500-660 ℃. The sintering temperature is too high, aluminum is likely to melt, and sintering fails; the sintering temperature is too low, and effective interface bonding cannot be formed between the powders.
As an embodiment of the present invention, the hot deformation process includes one or more of hot forging, hot rolling, hot extrusion. Wherein the thermal deformation processing temperature is 400-550 ℃.
The invention also relates to a ceramic reinforced aluminum-based composite material prepared by the brick-like bionic composite method.
The shape matching property of the micro-nano flaky powder adopted by the bricking-like bionic composite preparation process is realized, and the aluminum sheets and the ceramic sheets are alternately stacked in a bricking way, so that the ceramic reinforcement is uniformly dispersed in the middle of a matrix; meanwhile, the defects and energy stored in the sheet aluminum powder are few, and the structure and the performance are easy to keep stable in subsequent densification, sintering and thermal deformation processing. In contrast, in the traditional ceramic reinforced metal composite material, the ceramic reinforcement inevitably causes local hardening and stress concentration of the matrix while strengthening the matrix, and the high hardening state of the matrix reduces the plasticity of the matrix, so that the matrix is very easy to generate cracks in the stress or deformation process, rapidly expands in the hardened matrix and greatly reduces the toughness.
Compared with the prior art, the invention has the following beneficial effects:
(1) only short-time ball milling is needed to prepare micro-nano aluminum sheet elements;
(2) by utilizing the shape matching property between the micro-nano flaky powder, the aluminum sheets and the ceramic sheets are alternately stacked in a bricking way, so that the ceramic reinforcement is uniformly dispersed in the middle of a matrix;
(3) the thickness of the aluminum sheet and the ceramic sheet is only hundreds of nanometers, the structure and the scale effectively imitate a pearl layer structure, and the comprehensive mechanical property of the composite material is obviously improved compared with the conventional ceramic reinforced aluminum matrix composite material.
(4) The substrate of the brick-like bionic composite material presents an ultrafine grain layered structure, which is beneficial to dislocation motion in crystal grains, and the flaky ceramic sheet can also effectively block the expansion of cracks, thereby keeping high-strength plastic matching under the condition of fully exerting the dual mechanisms of ultrafine grain strengthening and crack deflection.
(5) The preparation method has wide application range, can prepare large alloy materials and is beneficial to large-scale production.
Drawings
Other features, objects and advantages of the invention will become more apparent upon reading of the detailed description of non-limiting embodiments with reference to the following drawings:
FIG. 1 is a schematic flow chart of the preparation process of the present invention;
FIG. 2 is a superfine crystal layered structure of a brick-type bionic composite material;
FIG. 3 is a metallographic structure diagram of an aluminum matrix composite prepared from (a) a flaky alumina and (b) an irregular alumina.
Detailed Description
The present invention will be described in detail with reference to specific examples. The following examples will assist those skilled in the art in further understanding the invention, but are not intended to limit the invention in any way. It should be noted that variations and modifications can be made by persons skilled in the art without departing from the spirit of the invention. All falling within the scope of the present invention.
The metal powders used in the following examples were all spray formed with a purity of greater than 99%. All the examples were carried out according to the process shown in FIG. 1, and the room-temperature mechanical properties of the materials in all the examples were carried out according to GB/T228.1-2010, with a drawing rate of 0.5 mm/min.
Example 1
Putting 100g of pure aluminum powder with the diameter of 10 mu m into a stirring type ball mill, taking absolute ethyl alcohol as a solvent, adding 4g of titanate as a ball milling auxiliary agent, ball-material ratio being 20:1, and carrying out ball milling for 5h at the rotating speed of 300 r/min to obtain flaky aluminum powder, wherein the flake diameter is about 25 mu m, and the flake thickness is about 300 nm;
60g of flaky alumina powder was mixed with 4.5g of flaky alumina powder having a thickness of 250nm and a diameter of 10 μm, and the mixed powder and 1Kg of agate balls were placed in 1L rolls, respectively, and then mixed at a speed of 50 rpm to uniformly mix the flaky alumina powder with the flaky alumina powder.
Finally, the mixed powder is pressed into a green body with the diameter of 40mm under the pressure of 200MPa, then the green body is sintered for 2 hours under the argon atmosphere at the temperature of 580 ℃, and then is rolled and formed at the temperature of 440 ℃, and the reduction is 80%.
The finally prepared material has the room-temperature tensile strength of 220MPa and the elongation of 20 percent. As can be seen from fig. 2, the brickmaking-like biomimetic composite material prepared in this example has an ultrafine grain layered structure.
Comparative example 1
60g of the flake powder prepared in example 1 was mixed with 4.5g of a conventional irregular alumina powder, wherein the average diameter of the conventional alumina used was 15 μm. The mixed powder and 1Kg of agate balls were placed in a 1L tumbler, respectively, and then mixed at a speed of 50 rpm to uniformly mix the flake-like aluminum powder with the irregular alumina powder.
Finally, the mixed powder is pressed into a green body with the diameter of 40mm under the pressure of 200MPa, then the green body is sintered for 2 hours under the argon atmosphere at the temperature of 580 ℃, and then is rolled and formed at the temperature of 440 ℃, and the reduction is 80%.
The tensile strength at room temperature of the finally prepared material is 205MPa, and the elongation is only 12%.
FIG. 3 is a metallographic structure diagram of a composite material prepared from flaky alumina and irregular alumina. The difference between them is the shape and arrangement of the reinforcement members. Compared with irregular alumina, the brick-like bionic composite material prepared from the flaky alumina has the advantages that the strength and the elongation are synchronously improved, and the high-strength plastic matching is kept.
Example 2
Placing 100g of pure aluminum powder with the diameter of 20 mu m in a stirring ball mill, taking absolute ethyl alcohol as a solvent, adding 4g of titanate as a ball milling auxiliary agent, ball-material ratio being 20:1, and carrying out ball milling for 8 hours at a rotating speed of 200 r/min to obtain flaky aluminum powder with the diameter of about 40 mu m and the thickness of about 200 nm;
60g of flaky aluminum powder and 10g of flaky alumina powder were mixed, wherein the flaky alumina used had a thickness of 250nm and a diameter of 10 μm, and the mixed powder and 1Kg of agate balls were placed in 1L rolls, respectively, and then mixed at a speed of 60 rpm to uniformly mix the flaky alumina powder and the flaky alumina powder.
And finally, pressing the mixed powder into a blank with the diameter of 40mm under the pressure of 200MPa, sintering the blank for 2 hours at the temperature of 600 ℃ in an argon atmosphere, and then rolling and forming at the temperature of 500 ℃ with the reduction of 80%.
The finally prepared material has the room-temperature tensile strength of 250MPa and the elongation of 18 percent.
Example 3
Putting 100g of pure aluminum powder with the diameter of 5 mu m into a stirring type ball mill, taking absolute ethyl alcohol as a solvent, adding 4g of titanate as a ball milling auxiliary agent, ball-material ratio being 20:1, and carrying out ball milling for 5h at the rotating speed of 300 r/min to obtain flaky aluminum powder, wherein the flake diameter is about 10 mu m, and the flake thickness is about 100 nm;
60g of aluminum flake powder and 10g of boron nitride flake powder are mixed, wherein the thickness of the used boron nitride flake is 100nm, the diameter of the boron nitride flake is 5 microns, the mixed powder and 1Kg of agate balls are respectively placed in a 1L roller, and then the aluminum flake powder and the boron nitride flake powder are mixed at the speed of 60 revolutions per minute to ensure that the aluminum flake powder and the boron nitride flake powder are uniformly mixed.
And finally, pressing the mixed powder into a blank with the diameter of 40mm under the pressure of 300MPa, sintering the blank for 2 hours at the temperature of 540 ℃ in an argon atmosphere, and then rolling and forming at the temperature of 300 ℃ with the reduction of 70%.
The finally prepared material has the room-temperature tensile strength of 240MPa and the elongation of 19 percent.
Example 4
Placing 100g of 6061 aluminum powder with the diameter of 10 mu m in a planetary ball mill, adding 4g of stearic acid as a ball milling aid, wherein the ball-material ratio is 20:1, and carrying out ball milling for 5 hours at the rotating speed of 300 r/min to obtain flaky aluminum powder, wherein the flake diameter is about 15 mu m, and the flake thickness is about 200 nm;
60g of flaky 6061 aluminum powder and 15g of flaky boron nitride powder are mixed, wherein the thickness of the flaky boron nitride is 150nm, the diameter of the flaky boron nitride is 10 microns, the mixed powder and 1Kg of agate balls are respectively placed in a 1L roller, and then the flaky aluminum powder and the flaky boron nitride powder are uniformly mixed at the speed of 60 revolutions per minute.
And finally, pressing the mixed powder into a blank with the diameter of 40mm under the pressure of 300MPa, sintering the blank for 2 hours at the temperature of 550 ℃ in an argon atmosphere, and then rolling and forming at the temperature of 400 ℃, wherein the reduction is 80%.
The tensile strength of the finally prepared material at room temperature is 360MPa, and the elongation is 12.5%.
The foregoing description of specific embodiments of the present invention has been presented. It is to be understood that the present invention is not limited to the specific embodiments described above, and that various changes and modifications may be made by one skilled in the art within the scope of the appended claims without departing from the spirit of the invention.

Claims (10)

1. A method for preparing a ceramic reinforced aluminum-based composite material by brick-like bionic composite is characterized by comprising the following steps:
(1) preparing micro-nano aluminum sheet elements: ball-milling spherical aluminum powder to obtain micro-nano flaky aluminum powder with preferred orientation;
(2) uniformly mixing the micro-nano aluminum sheet element and the flaky ceramic reinforcement element by adopting a roller powder mixing mode;
(3) carrying out densification treatment to obtain a brick-like bionic composite powder ingot blank;
(4) and sintering and thermally deforming the powder ingot blank to obtain the brick-like bionic composite ceramic reinforced aluminum-based composite material.
2. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like type biomimetic composite according to claim 1, wherein the ball milling adopts parameters as follows: the mass ratio of the steel balls to the aluminum powder is 10: 1-30: 1, the rotating speed is 50-400 r/min, and the time is 2-10 h.
3. The method for preparing the ceramic reinforced aluminum matrix composite material by the brick-like bionic composite method according to claim 1, wherein the thickness of the micro-nano aluminum sheet element is 0.2-0.5 μm, and the sheet diameter is 5-50 μm.
4. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite method according to claim 1, wherein the thickness of the flaky ceramic reinforcement element is 0.2-0.5 μm, and the diameter is 5-30 μm.
5. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite method according to claim 1, wherein in the roller powder mixing mode, the mass ratio of the agate balls to the powder is 2: 1-20: 1, the rotating speed is as follows: 5-100 rpm.
6. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite method according to claim 1, wherein the volume fraction of the flaky ceramic reinforcement in the composite material is 1-30 vol.%.
7. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite method according to claim 1, wherein the densification treatment adopts a cold pressing process, wherein the cold pressing temperature is 20-200 ℃, and the pressure is 300-500 MPa.
8. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite method according to claim 1, wherein the sintering process is vacuum hot-pressing sintering, atmosphere sintering, spark ion beam sintering and hot isostatic pressing sintering; and the sintering temperature is 500-660 ℃. The sintering temperature is too high, aluminum is likely to melt, and sintering fails; the sintering temperature is too low, and effective interface bonding cannot be formed between the powders.
9. The method for preparing the ceramic reinforced aluminum-based composite material by the brick-like bionic composite method according to claim 1, wherein the thermal deformation processing comprises one or more of hot forging, hot rolling and hot extrusion.
10. A brick-like biomimetic composite prepared ceramic reinforced aluminum matrix composite material prepared according to the method of any of claims 1-9.
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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115010100A (en) * 2022-06-21 2022-09-06 西安交通大学 Flaky aluminum nitride powder and preparation method thereof

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