CN110229979B - Intragranular grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material and preparation method thereof - Google Patents

Intragranular grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material and preparation method thereof Download PDF

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CN110229979B
CN110229979B CN201910603589.7A CN201910603589A CN110229979B CN 110229979 B CN110229979 B CN 110229979B CN 201910603589 A CN201910603589 A CN 201910603589A CN 110229979 B CN110229979 B CN 110229979B
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刘志伟
董志武
郑巧玲
皇志富
高义民
邢建东
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Xianyang Gazelle Valley New Material Technology Co ltd
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Xian Jiaotong University
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    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1005—Pretreatment of the non-metallic additives
    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
    • 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

Abstract

The invention discloses an intracrystalline grain boundary distribution microA nano-class multi-phase particle reinforced Al-base composite material is prepared through preparing K2TiF6Adding the powder into the pure aluminum melt, and preparing the Al-Al with uniform tissue by ultrasonic stirring3Ti master alloy, and Al-Al obtained3Al in Ti intermediate alloy3The average particle size of Ti particles is less than 5 μm; then K is put2TiF6Powder and KBF4Mixing the powder according to the molar ratio of 1:2, adding the mixture into a pure aluminum melt, and performing ultrasonic stirring treatment to prepare Al-TiB with uniform tissue2Master alloy, and Al-TiB obtained2Intermediate alloy of TiB2The average particle size of the particles is less than 100 nm; finally, Al-Al3Ti master alloy and Al-TiB2The intermediate alloy is used as raw material, or Al, alloy element, Al-Al3Ti master alloy and Al-TiB2And (3) taking the intermediate alloy as a raw material, melting the raw material, dispersing the reinforced particles by ultrasonic stirring, and pouring to obtain the intragranular crystal boundary dual-reinforced aluminum-based composite material.

Description

Intragranular grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material and preparation method thereof
Technical Field
The invention belongs to the field of advanced metal matrix composite material preparation, and particularly relates to an ultrasonic-assisted liquid phase composite method for preparing an intragranular grain boundary distribution small-grain size complex-phase particle reinforced aluminum matrix composite material and a preparation method thereof.
Background
The particle reinforced aluminum matrix composite material has high specific strength, high specific modulus and good wear resistance, and has very wide application prospect in the fields of aerospace, automobile manufacturing, electronic devices and the like. The preparation method of the particle reinforced aluminum matrix composite material by adopting the casting method can obviously reduce the production cost and can directly obtain a casting with a complex shape, so the method has great attention in the field of preparation of the particle reinforced aluminum matrix composite material. Generally, the smaller the particle size of the reinforcing particles, the more pronounced the reinforcing effect thereof; the higher the dispersibility of the reinforced particles, the more excellent the macroscopic mechanical properties of the material. However, the distribution of a single small-particle-size reinforcing phase in the aluminum melt has a significant tendency in solidification, which easily causes particle segregation (for example, ceramic particles are mostly segregated at an alpha-Al crystal boundary, and the smaller the particle size is, the more serious the segregation is), seriously reduces the ductility and toughness of the material, causes potential safety hazards in use, and limits the popularization and use of the material.
Disclosure of Invention
The invention aims to provide an intragranular grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material and a preparation method thereof, which aim to overcome the problems in the prior art. The invention can realize the controllable preparation of the subsequent composite material (the content of the reinforced particles in the composite material is controllable), thereby obtaining the grain boundary distribution micro-nano grain diameter Al in the crystal3Ti particles/TiB2The particles reinforce the Al-based composite material.
In order to achieve the purpose, the invention adopts the following technical scheme:
in-crystal grain boundary distribution micro-nano grain diameter Al3Ti particles/TiB2A preparation method of a particle-reinforced Al-based composite material comprises the step of respectively preparing Al-Al by utilizing ultrasonic-assisted molten salt reaction3Ti、Al-TiB2Master alloys in which Al is grown in situ3Ti、TiB2The average sizes of the particles are respectively micron particle size and nanometer particle size, then the intra-crystalline grain boundary distribution micro-nano particle size Al is obtained after the remelting dilution process and the ultrasonic stirring are assisted, and the casting3Ti particles/TiB2The particles reinforce the Al-based composite material.
The method specifically comprises the following steps:
a preparation method of an intragranular crystal boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material comprises the following steps:
step 1: will K2TiF6Adding the powder into the pure aluminum melt, and preparing the Al-Al with uniform tissue by ultrasonic stirring3Ti master alloy, and Al-Al obtained3Al in Ti intermediate alloy3The average particle size of Ti particles is less than 5 μm;
step 2: will K2TiF6Powder and KBF4Mixing the powder according to the molar ratio of 1:2, adding the mixture into a pure aluminum melt, and performing ultrasonic stirring treatment to prepare Al-TiB with uniform tissue2Master alloy, and Al-TiB obtained2Intermediate alloy of TiB2The average particle size of the particles is less than 100 nm;
and step 3: al, Al-Al obtained in step 13Ti intermediate alloy and Al-TiB obtained in step 22Taking an intermediate alloy as a raw material, or taking Al, alloy elements and the Al-Al obtained in the step 13Ti intermediate alloy and Al-TiB obtained in step 22And (3) taking the intermediate alloy as a raw material, melting the raw material, dispersing the reinforced particles by ultrasonic stirring, and pouring to obtain the intragranular crystal boundary dual-reinforced aluminum-based composite material.
Further, the pure Al melt temperature in step 1 is 700-.
Further, the ultrasonic agitation treatment in the step 1 specifically comprises: and immersing an ultrasonic amplitude rod made of Nb-Zr alloy into the melt, wherein the ultrasonic treatment time is 5-10min, and the ultrasonic power is 0.5-1.5 kW.
Further, Al-Al obtained in step 13Al in Ti intermediate alloy3The mass fraction of Ti particles is less than or equal to 15 percent.
Further, the pure Al melt temperature in step 2 is 700-.
Further, the ultrasonic agitation treatment in the step 2 specifically comprises: and immersing an ultrasonic amplitude rod made of Nb-Zr alloy into the melt, wherein the ultrasonic treatment time is 5-10min, and the ultrasonic power is 0.5-1.5 kW.
Further, Al-TiB obtained in step 22Intermediate alloy of TiB2The mass fraction of the particles is less than or equal to 15 percent.
Further, the raw material in step 3 was melted at 800 ℃ and 700 ℃.
Further, the ultrasonic agitation treatment in the step 3 specifically comprises: and immersing an ultrasonic amplitude rod made of Nb-Zr alloy into the melt, wherein the ultrasonic treatment time is 5-10min, and the ultrasonic power is 0.5-1.5 kW.
An intragranular grain boundary distribution micro-nano multiphase particle reinforced aluminum matrix composite is prepared by the preparation method of the intragranular grain boundary distribution micro-nano multiphase particle reinforced aluminum matrix composite.
Compared with the prior art, the invention has the following beneficial technical effects:
the invention prepares Al-Al by utilizing ultrasonic-assisted molten salt reaction3A Ti intermediate alloy, a Ti intermediate alloy and a Ti intermediate alloy,cavitation and acoustic flow effects generated in the aluminum melt by high-strength ultrasound can remarkably accelerate the reaction process, and massive Al with the average grain diameter less than 5 mu m can be synthesized at low temperature (less than 800 ℃) and in short time (less than 10min)3Ti particles and Al3The yield of Ti particles can reach more than 95 percent. While the traditional method for preparing Al without ultrasonic assistance3The melt temperature of Ti particles is higher than 800 ℃, and Al with a large-size (the length is more than 10 mu m) rod-shaped structure is easily obtained3Ti particles. Preparation of Al-TiB by ultrasonic-assisted molten salt reaction2The intermediate alloy can synthesize TiB with average grain diameter less than 100nm at lower temperature (less than 850 ℃) in shorter time (less than 10min)2Particles of and TiB2The yield of the particles can reach more than 90% (no other impurity phase exists). Preparation of TiB by traditional ultrasonic-assisted-free molten salt reaction2The temperature of the particle melt needs to be higher than 850 ℃, and the reaction time needs to be more than 30min (in order to ensure TiB)2Synthesis rate of particles) to obtain TiB2The particle size is submicron and micron particle size. Therefore, the adoption of ultrasonic assistance can obviously reduce Al3Ti and TiB2The grain size and the production cost can be effectively reduced. In addition, the stirring effect generated by the ultrasonic in the aluminum melt can effectively break the Al3Ti、TiB2The particle agglomeration and the ultrasonic cavitation effect can obviously improve Al3Ti、TiB2The particles and the aluminum melt are fully dispersed in the melt due to the wettability, the ultrasonic treatment has the functions of degassing and impurity removal, and Al-Al with uniform structure and less pores/inclusions can be obtained after casting3Ti and Al-TiB2And (3) intermediate alloy. The result can realize the controllable preparation of the subsequent composite material (the content of the reinforced particles in the composite material is controllable), thereby obtaining the grain boundary distribution micro-nano grain diameter Al in the crystal3Ti particles/TiB2The particles reinforce the Al-based composite material.
The ultrasonic amplitude rod used in the invention is made of Nb-Zr alloy material, and has more stability (the solubility of niobium in the aluminum melt is extremely low) in the aluminum melt compared with the traditional Ti alloy, and can effectively avoid introducing other alloy elements into the aluminum melt.
Drawings
FIG. 1 shows Al-Al prepared in example 13TiPhase XRD pattern (a) of intermediate alloy, microstructure photo (b) and in-situ generated Al3The particle size distribution (c) of Ti particles.
FIG. 2 shows Al-TiB prepared in example 12Phase XRD pattern (a) of intermediate alloy, microstructure photo (b) and in-situ generated TiB2The particle size distribution (c) of the particles.
FIG. 3 shows the grain boundary distribution micro-nano grain diameter Al in the crystal prepared in example 13Ti particles/TiB2Microstructure photograph (a: 200X; b: 500X) of the particle-reinforced Al-based composite material.
Detailed Description
The invention is described in further detail below:
the invention discloses a preparation method of an intracrystalline grain boundary distribution micro-nano multiphase particle reinforced aluminum matrix composite material2TiF6-Al、K2TiF6/KBF4Al) to respectively prepare Al-Al with uniform structure3Ti、Al-TiB2Master alloys in which Al is grown in situ3Ti、TiB2The average particle diameters of the particles are less than 5 μm and 100nm, respectively. With Al-Al3Ti、Al-TiB2The intermediate alloy, Al and alloy elements are used as raw materials, or Al-Al is used3Ti、Al-TiB2Taking intermediate alloy and Al as raw materials, and diluting micron Al by using the intermediate alloy3Ti particles and nano TiB2The particles are introduced into an aluminum (alloy) matrix, and are stirred with ultrasound, and then are poured into a mold, so that the micro-nano complex phase particle reinforced aluminum matrix composite material with the grain boundary distribution in the crystal is obtained.
The method specifically comprises the following steps:
step 1: will K2TiF6Adding the powder into a 700-plus 800 ℃ pure aluminum melt, performing ultrasonic stirring treatment to remove liquid molten salt impurities on the surface of the melt, and preparing Al-Al with uniform tissue after pouring3Ti master alloy, in situ endogenetic Al3Ti particles having an average particle diameter of less than 5 μm, and Al-Al obtained3Al in Ti intermediate alloy3The mass fraction of Ti particles is less than or equal to 15 percent.
Step 2: will K2TiF6、KBF4Mixing the powder according to the molar ratio of 1:2, adding the mixed powder into a pure aluminum melt with the temperature of 700-plus-one 850 ℃, performing ultrasonic stirring treatment to remove liquid molten salt impurities on the surface of the melt, and preparing Al-TiB with uniform tissue after pouring2Master alloy, in situ endogeneous TiB2The average particle diameter of the particles is less than 100nm, and the obtained Al-TiB2Intermediate alloy of TiB2The mass fraction of the particles is less than or equal to 15 percent.
And step 3: al and Al-Al prepared in step 1 and step 23Ti、Al-TiB2Taking an intermediate alloy as a raw material, or taking Al, alloy elements and Al-Al prepared in the step 1 and the step 23Ti、Al-TiB2The intermediate alloy is used as raw material, in which the alloy elements are Si, Mg, Cu, etc. (alloy elements commonly used for casting and deforming aluminium alloy), and different Al can be prepared by regulating and controlling the proportion3Ti、TiB2The aluminum-based composite material with the particle content is prepared by melting raw materials at the temperature of 700-.
The adding mode of ultrasonic auxiliary stirring adopted in the steps 1, 2 and 3 is as follows: immersing an ultrasonic amplitude rod made of Nb-Zr alloy into the melt, wherein the ultrasonic treatment time is 5-10min, the ultrasonic power is 0.5-1.5kW, and the K is controlled in the step 12TiF6The addition amount of the powder can be used for preparing different Al3Al-Al of Ti particle content3Ti master alloy, control of K in step 22TiF6、KBF4The addition amount of the powder can be used for preparing different TiB2Particle content of Al-TiB2And (3) intermediate alloy.
It should be noted that, the final composite material matrix may contain different amounts of alloy elements according to specific situations.
The present invention is described in detail below with reference to examples:
example 1
Step 1: will K2TiF6Adding the powder into a pure aluminum melt with the temperature of 750 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 10min with the ultrasonic power of 1.2kW, removing liquid molten salt impurities on the surface of the melt, and pouringTo obtain Al-Al3Ti master alloy, Al-Al obtained3Al in Ti intermediate alloy3The mass fraction of Ti particles is 10%.
Step 2: will K2TiF6、KBF4Mixing the powder according to a molar ratio of 1:2, fully mixing, adding the mixture into a pure aluminum melt at the temperature of 800 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 10min with the ultrasonic power of 1.2kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-TiB2Master alloy, Al-TiB obtained2Intermediate alloy of TiB2The mass fraction of the particles was 10%.
And step 3: al and Al-Al prepared in step 1 and step 23Ti、Al-TiB2Taking the master alloy as a raw material, adding Si and Mg elements, and preparing 2 wt.% Al3Ti+3wt.％TiB2Melting the Al-7Si-0.4Mg composite material at 730 ℃, carrying out ultrasonic treatment for 5min, wherein the ultrasonic power is 1.2kW, and pouring to obtain the micro-nano complex phase particle reinforced aluminum matrix composite material with the grain boundary distribution in the crystal.
FIG. 1 shows Al-10 wt.% Al prepared using an ultrasound-assisted molten salt reaction3Ti intermediate alloy has no other impurity phase generated (a) and the intermediate alloy has even microstructure (b), (c) in-situ generated Al3The average particle diameter of the Ti particles is less than 5 μm.
FIG. 2 shows Al-10 wt.% TiB prepared using an ultrasound-assisted molten salt reaction2The master alloy has no other impurity phase generated (a) and the microstructure of the master alloy is uniform (b), (c) the in-situ generated TiB2The particles have an average particle size of less than 100 nm.
FIG. 3 shows that in the complex phase reinforced aluminum matrix composite, the micron Al3Ti particles are mostly positioned in alpha-Al crystal, and nano TiB2The particles are mainly located at the alpha-Al grain boundaries.
Example 2
Step 1: will K2TiF6Adding the powder into a pure aluminum melt with the temperature of 800 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 5min with the ultrasonic power of 1.5kW, removing liquid molten salt impurities on the surface of the melt, and obtaining Al-Al after pouring3A Ti intermediate alloy, a Ti intermediate alloy and a Ti intermediate alloy,the obtained Al-Al3Al in Ti intermediate alloy3The mass fraction of Ti particles was 15%.
Step 2: will K2TiF6、KBF4Mixing the powder according to a molar ratio of 1:2, fully mixing, adding the mixture into a pure aluminum melt with the temperature of 850 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 5min with the ultrasonic power of 1.2kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-TiB2Master alloy, Al-TiB obtained2Intermediate alloy of TiB2The mass fraction of the particles was 15%.
And step 3: al and Al-Al prepared in step 1 and step 23Ti、Al-TiB2Taking the master alloy as a raw material, adding Si and Mg elements, and preparing 1 wt.% Al3Ti+4wt.％TiB2Melting the Al-7Si-0.4Mg composite material at 750 ℃, carrying out ultrasonic treatment for 5min, wherein the ultrasonic power is 1.2kW, and pouring to obtain the micro-nano complex phase particle reinforced aluminum matrix composite material with the grain boundary distribution in the crystal.
Example 3
Step 1: will K2TiF6Adding the powder into a pure aluminum melt with the temperature of 700 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 10min with the ultrasonic power of 1.0kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-Al3Ti master alloy, Al-Al obtained3Al in Ti intermediate alloy3The mass fraction of Ti particles was 8%.
Step 2: will K2TiF6、KBF4Mixing the powder according to a molar ratio of 1:2, fully mixing, adding the mixture into a pure aluminum melt at the temperature of 750 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 8min with the ultrasonic power of 1.5kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-TiB2Master alloy, Al-TiB obtained2Intermediate alloy of TiB2The mass fraction of the particles was 8%.
And step 3: al and Al-Al prepared in step 1 and step 23Ti、Al-TiB2The intermediate alloy is taken as a raw material, and Cu element is added,1 wt.% Al is prepared3Ti+4wt.％TiB2Melting the Al-4.5Cu composite material at 700 ℃, carrying out ultrasonic treatment for 10min, wherein the ultrasonic power is 1.2kW, and pouring to obtain the intra-grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material.
Example 4
Step 1: will K2TiF6Adding the powder into a pure aluminum melt with the temperature of 700 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 8min with the ultrasonic power of 1.0kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-Al3Ti master alloy, Al-Al obtained3Al in Ti intermediate alloy3The mass fraction of Ti particles is 10%.
Step 2: will K2TiF6、KBF4Mixing the powder according to the molar ratio of 1:2, fully mixing, adding the mixture into a pure aluminum melt at the temperature of 700 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 10min with the ultrasonic power of 1.5kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-TiB2Master alloy, Al-TiB obtained2Intermediate alloy of TiB2The mass fraction of the particles was 10%.
And step 3: al and Al-Al prepared in step 1 and step 23Ti、Al-TiB2Preparing 3 wt.% Al by using the intermediate alloy as a raw material3Ti+2wt.％TiB2Melting the/Al composite material at 750 ℃, carrying out ultrasonic treatment for 5min, wherein the ultrasonic power is 1.5kW, and pouring to obtain the micro-nano complex phase particle reinforced aluminum matrix composite material with the grain boundary distribution in the crystal.
Example 5
Step 1: will K2TiF6Adding the powder into a pure aluminum melt with the temperature of 800 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 5min with the ultrasonic power of 0.5kW, removing liquid molten salt impurities on the surface of the melt, and obtaining Al-Al after pouring3Ti master alloy, Al-Al obtained3Al in Ti intermediate alloy3The mass fraction of Ti particles is 10%.
Step 2: will K2TiF6、KBF4Powder according to moleMixing materials according to the ratio of 1:2, fully mixing, adding into a pure aluminum melt with the temperature of 850 ℃, simultaneously immersing an Nb-Zr alloy ultrasonic amplitude rod into the melt, carrying out ultrasonic treatment for 10min with the ultrasonic power of 0.5kW, removing liquid molten salt impurities on the surface of the melt, and pouring to obtain Al-TiB2Master alloy, Al-TiB obtained2Intermediate alloy of TiB2The mass fraction of the particles was 10%.
And step 3: al and Al-Al prepared in step 1 and step 23Ti、Al-TiB2Taking the intermediate alloy as a raw material, and preparing 2 wt.% of Al3Ti+3wt.％TiB2Melting the/Al composite material at 800 ℃, carrying out ultrasonic treatment for 8min, wherein the ultrasonic power is 0.5kW, and pouring to obtain the micro-nano complex phase particle reinforced aluminum matrix composite material with the grain boundary distribution in the crystal.

Claims (4)

1. A preparation method of an intragranular crystal boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material is characterized by comprising the following steps:
step 1: will K2TiF6Adding the powder into a pure aluminum melt with the temperature of 700 plus 800 ℃, and preparing the Al-Al with uniform tissue by ultrasonic stirring3Ti master alloy, and Al-Al obtained3Al in Ti intermediate alloy3The average particle size of Ti particles is less than 5 μm;
step 2: will K2TiF6Powder and KBF4The powder is mixed according to the molar ratio of 1:2, then is added into pure aluminum melt with the temperature of 700-2Master alloy, and Al-TiB obtained2Intermediate alloy of TiB2The average particle size of the particles is less than 100 nm;
and step 3: al, Al-Al obtained in step 13Ti intermediate alloy and Al-TiB obtained in step 22Taking an intermediate alloy as a raw material, or taking Al, alloy elements and the Al-Al obtained in the step 13Ti intermediate alloy and Al-TiB obtained in step 22The master alloy is used as a raw material, the raw material is melted at the temperature of 700-;
wherein the ultrasonic stirring treatment in the step 1, the step 2 and the step 3 is specifically as follows: and immersing an ultrasonic amplitude rod made of Nb-Zr alloy into the melt, wherein the ultrasonic treatment time is 5-10min, and the ultrasonic power is 0.5-1.5 kW.
2. The method for preparing the micro-nano complex phase particle reinforced aluminum matrix composite material with the grain boundary distribution in the crystal according to claim 1, wherein the Al-Al obtained in the step 13Al in Ti intermediate alloy3The mass fraction of Ti particles is less than or equal to 15 percent.
3. The method for preparing an intra-crystal grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material according to claim 1, wherein the Al-TiB obtained in the step 22Intermediate alloy of TiB2The mass fraction of the particles is less than or equal to 15 percent.
4. An in-crystal grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material, which is characterized by being prepared by the preparation method of the in-crystal grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material according to any one of claims 1 to 3.
CN201910603589.7A 2019-07-05 2019-07-05 Intragranular grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material and preparation method thereof Active CN110229979B (en)

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