CN117226086A - High-strength plastic multiphase heterogeneous titanium-based composite material and preparation method thereof - Google Patents
High-strength plastic multiphase heterogeneous titanium-based composite material and preparation method thereof Download PDFInfo
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- 239000002131 composite material Substances 0.000 title claims abstract description 202
- 239000010936 titanium Substances 0.000 title claims abstract description 155
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 112
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 112
- 238000002360 preparation method Methods 0.000 title claims abstract description 21
- 239000000843 powder Substances 0.000 claims abstract description 168
- 229910021393 carbon nanotube Inorganic materials 0.000 claims abstract description 150
- 239000010949 copper Substances 0.000 claims abstract description 111
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 91
- 239000002041 carbon nanotube Substances 0.000 claims abstract description 90
- 238000000498 ball milling Methods 0.000 claims abstract description 76
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 48
- 230000002902 bimodal effect Effects 0.000 claims abstract description 43
- 239000011159 matrix material Substances 0.000 claims abstract description 39
- 239000002245 particle Substances 0.000 claims abstract description 34
- 238000000034 method Methods 0.000 claims abstract description 23
- 238000005245 sintering Methods 0.000 claims abstract description 22
- JPVYNHNXODAKFH-UHFFFAOYSA-N Cu2+ Chemical compound [Cu+2] JPVYNHNXODAKFH-UHFFFAOYSA-N 0.000 claims abstract description 11
- 150000001875 compounds Chemical class 0.000 claims abstract description 10
- 229910001431 copper ion Inorganic materials 0.000 claims abstract description 10
- 238000005098 hot rolling Methods 0.000 claims abstract description 10
- 238000002156 mixing Methods 0.000 claims description 28
- 239000011858 nanopowder Substances 0.000 claims description 22
- 239000000463 material Substances 0.000 claims description 20
- HEMHJVSKTPXQMS-UHFFFAOYSA-M Sodium hydroxide Chemical compound [OH-].[Na+] HEMHJVSKTPXQMS-UHFFFAOYSA-M 0.000 claims description 15
- 238000001354 calcination Methods 0.000 claims description 14
- 229910052739 hydrogen Inorganic materials 0.000 claims description 9
- 239000001257 hydrogen Substances 0.000 claims description 9
- 230000002787 reinforcement Effects 0.000 claims description 8
- 229910000365 copper sulfate Inorganic materials 0.000 claims description 7
- ARUVKPQLZAKDPS-UHFFFAOYSA-L copper(II) sulfate Chemical compound [Cu+2].[O-][S+2]([O-])([O-])[O-] ARUVKPQLZAKDPS-UHFFFAOYSA-L 0.000 claims description 7
- 238000001035 drying Methods 0.000 claims description 7
- 230000007935 neutral effect Effects 0.000 claims description 7
- 239000002243 precursor Substances 0.000 claims description 7
- 239000002994 raw material Substances 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 7
- 239000000243 solution Substances 0.000 claims description 6
- KWYUFKZDYYNOTN-UHFFFAOYSA-M Potassium hydroxide Chemical compound [OH-].[K+] KWYUFKZDYYNOTN-UHFFFAOYSA-M 0.000 claims description 4
- 239000012670 alkaline solution Substances 0.000 claims description 4
- OPQARKPSCNTWTJ-UHFFFAOYSA-L copper(ii) acetate Chemical compound [Cu+2].CC([O-])=O.CC([O-])=O OPQARKPSCNTWTJ-UHFFFAOYSA-L 0.000 claims description 4
- XTVVROIMIGLXTD-UHFFFAOYSA-N copper(II) nitrate Chemical compound [Cu+2].[O-][N+]([O-])=O.[O-][N+]([O-])=O XTVVROIMIGLXTD-UHFFFAOYSA-N 0.000 claims description 2
- 238000000465 moulding Methods 0.000 claims description 2
- 238000004321 preservation Methods 0.000 claims description 2
- 238000001132 ultrasonic dispersion Methods 0.000 claims description 2
- 239000013078 crystal Substances 0.000 abstract description 12
- 238000009825 accumulation Methods 0.000 abstract description 5
- 238000012986 modification Methods 0.000 abstract description 4
- 230000004048 modification Effects 0.000 abstract description 4
- 238000005554 pickling Methods 0.000 abstract description 3
- 238000004519 manufacturing process Methods 0.000 abstract description 2
- 238000007780 powder milling Methods 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 19
- 239000012071 phase Substances 0.000 description 10
- 239000010935 stainless steel Substances 0.000 description 10
- 229910001220 stainless steel Inorganic materials 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- 230000008569 process Effects 0.000 description 8
- 238000009792 diffusion process Methods 0.000 description 6
- 230000003014 reinforcing effect Effects 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 238000001816 cooling Methods 0.000 description 5
- 238000010586 diagram Methods 0.000 description 5
- 239000002082 metal nanoparticle Substances 0.000 description 5
- 230000008901 benefit Effects 0.000 description 4
- 239000007795 chemical reaction product Substances 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 238000011065 in-situ storage Methods 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000008595 infiltration Effects 0.000 description 3
- 238000001764 infiltration Methods 0.000 description 3
- 150000002500 ions Chemical class 0.000 description 3
- 238000011068 loading method Methods 0.000 description 3
- 239000002105 nanoparticle Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- BICXKAQZWLCDDX-UHFFFAOYSA-N copper dinitrate pentahydrate Chemical compound O.O.O.O.O.[Cu+2].[O-][N+]([O-])=O.[O-][N+]([O-])=O BICXKAQZWLCDDX-UHFFFAOYSA-N 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000003786 synthesis reaction Methods 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000001010 compromised effect Effects 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 125000000524 functional group Chemical group 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000006317 isomerization reaction Methods 0.000 description 1
- 238000009766 low-temperature sintering Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000011156 metal matrix composite Substances 0.000 description 1
- 229910021392 nanocarbon Inorganic materials 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000012779 reinforcing material Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000001778 solid-state sintering Methods 0.000 description 1
- 238000001179 sorption measurement Methods 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention discloses a high-strength plastic multiphase heterogeneous titanium-based composite material and a preparation method thereof, wherein the method comprises the following steps: 1. selecting small-particle-size and large-particle-size spherical titanium alloy powder, pickling carbon nano tubes and soluble copper ion-containing compounds; 2. preparing Cu@CNTs composite powder and ball-milling the Cu@CNTs composite powder with small-particle-size spherical titanium alloy powder to obtain heterogeneous Cu@CNTs/titanium-based composite powder; 3. ball milling with large-grain-size spherical titanium alloy powder to obtain bimodal heterogeneous Cu@CNTs/titanium-based composite powder; 4. and hot rolling after sintering and forming by using the spark plasma. The invention adopts Cu doped CNTs for modification, combines titanium alloy powder with different particle diameters to construct a double-peak matrix of coarse crystals and fine crystals, and regulates and controls inter-crystal nano TiC and intra-crystal Ti 2 Cu is generated, the accumulation of geometrically necessary dislocation is promoted, the strength of the titanium-based composite material is improved, the plasticity of the titanium-based composite material is optimized, the high strength-high plasticity matching of the titanium-based composite material is realized, the preparation process is easy to realize, and the method is suitable for industrial mass production.
Description
Technical Field
The invention relates to the technical field of configuration design and preparation of metal matrix composite materials, in particular to a high-strength plastic multiphase heterogeneous titanium matrix composite material and a preparation method thereof.
Background
In recent years, the titanium-based composite materials (TMCs) with light weight and high strength as the metal structural parts have wide application prospects in the fields of aviation and weaponry. To overcome the limitations of the traditional ceramic reinforcing phase, ultra-high strength nanocarbon materials have been widely accepted as a new generation of reinforcing materials for TMCs. As representative one-dimensional Carbon Nanotubes (CNTs), the TMCs have the advantages and also have some defects, such as poor affinity between CNTs and Ti, incompatible surface tension and specific surface energy, and weak wettability of CNTs-Ti interface, thereby seriously affecting the toughening performance of CNTs/Ti composite materials and limiting the development and practical application thereof.
To solve the above problems, the direct interface reaction product Ti between CNTs and Ti x C y As a transition layer, it is considered that the wettability of the CNTs/Ti interface is enhanced, and Ti x C y Will lock CNTs under mechanical load, transfer CNTs' load asThe exertion is maximized to improve the material force. However, when the sintering temperature is too low, a small amount of interface reaction products are insufficient to enhance the wettability of CNTs-Ti interfaces, and the density of the CNTs/Ti composite material obtained by low-temperature sintering is low, so that the strong plasticity improving effect of the material is poor. When the sintering temperature is too high, the transition layer formed by excessive interface reaction products can effectively improve the wettability of CNTs-Ti interfaces, but greatly sacrifice the plasticity of the CNTs/Ti composite material due to brittleness. In addition, no matter the sintering temperature is high or low, the generated Ti x C y The structural integrity of the CNTs is inevitably compromised, thereby increasing the non-uniformity of the CNTs microstructure, resulting in partial enhancement performance loss of the CNTs. Therefore, the direct interface reaction is used for improving the wettability of the CNTs-Ti interface so as to further improve the strength and the plasticity of the CNTs/Ti composite material.
Surface modification of CNTs is an effective strategy to promote interfacial infiltration. By loading the metal nano particles on the CNTs tube wall through various methods, not only can the interfacial wettability of the CNTs/Ti composite powder be improved by virtue of the good wettability of the metal nano particles, but also the doped CNTs are more uniformly distributed on the surface of the Ti matrix powder because the density of the doped CNTs is far higher than that of undoped CNTs. Furthermore, the metal nano particles can exert the advantage of self rapid diffusion in the sintering and forming process, activate the self diffusion effect of Ti, generate intermetallic compound precipitate phases in CNTs/Ti interfaces or Ti matrix crystals, and realize the effect of improving the sinterability and the forcefulness of TMCs. However, the CNTs structure is inevitably destroyed during sintering, and the CNTs are partially enhanced, so that plastic optimization cannot be realized.
Disclosure of Invention
The technical problem to be solved by the invention is to provide a preparation method of a high-strength plastic multiphase heterogeneous titanium-based composite material aiming at the defects of the prior art. On the basis of adopting Cu doping modification strategy on the surface of CNTs, the method utilizes titanium alloy powder with different particle diameters to construct a double-peak matrix, so that CNTs are fully reacted in a sintering mode to generate nano TiC, and the inter-crystal nano TiC and the intra-crystal Ti are regulated and controlled 2 Cu is generated, the strength of the titanium-based composite material is improved, and coarse grains and fine grains are promotedThe geometrical necessary dislocation accumulation caused by the incompatibility of plastic deformation between the titanium-based alloy powder and the titanium-based alloy powder optimizes the plasticity of the titanium-based composite material, obtains the titanium-based composite material with excellent strong plasticity matching, and solves the problems of uneven distribution of CNTs on the surface of the Ti-based alloy powder, poor interface wettability and 'inversion' of the toughness of the conventional metal material.
In order to solve the technical problems, the invention adopts the following technical scheme: the preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized by comprising the following steps of:
step one, selecting raw materials: respectively selecting small-particle-size spherical titanium alloy powder and large-particle-size spherical titanium alloy powder prepared by a rotating electrode method as matrix materials, and selecting acid-washed carbon nano tubes and soluble copper ion-containing compounds as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing the acid-washed carbon nano tube and the soluble copper ion-containing compound in the first step by ultrasonic, dripping an alkaline solution to adjust the pH value to be neutral, standing, drying the obtained nano powder, calcining and reducing the nano powder in an argon-hydrogen atmosphere to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, and placing the Cu@CNTs composite powder and the small-particle-size spherical titanium alloy powder selected in the first step in a planetary ball mill for ball milling and mixing uniformly to obtain the isomeric titanium-based composite powder which is marked as the isomeric Cu@CNTs/titanium-based composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing the heterogeneous Cu@CNTs/titanium-based composite powder prepared in the second step and the large-particle-size spherical titanium alloy powder selected in the first step into a planetary ball mill for ball milling and mixing uniformly to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/titanium-based composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: carrying out hot rolling on the bimodal isomerism Cu@CNTs/titanium matrix composite powder prepared in the step three after discharge plasma sintering molding to obtain a multiphase isomerism titanium matrix composite material, and marking the multiphase isomerism Cu@CNTs/titanium matrix composite material; the room-temperature tensile strength of the heterogeneous titanium-based composite material is 1160-1506 MPa, and the elongation after fracture is 9-12.5%.
The invention firstly adopts CNTs and soluble copper ion-containing compounds to form copper doped carbon nano tube composite powder through calcination and reduction, then carries out ball milling on the composite powder and small-particle-size spherical titanium alloy powder to prepare heterogeneous Cu@CNTs/titanium base composite powder, then carries out ball milling on the obtained composite powder and large-particle-size spherical titanium alloy powder, can regulate the content ratio of the two, and finally obtains the high-strength plastic heterogeneous titanium base composite material through solid phase sintering, bonding and deformation processing.
Compared with undoped CNTs, the invention adopts Cu doped CNTs, improves the interface bonding degree of the CNTs and the Ti-based composite powder by utilizing the good infiltration capacity of Cu particles, and because the density of the Cu doped CNTs is far higher than that of undoped CNTs, the CNTs are more uniformly distributed on the surface of the Ti-based composite powder, thereby the Cu particles exert the advantage of self rapid diffusion in the sintering forming process of the Ti-based composite powder added with the Cu doped CNTs, activate the self-diffusion effect of Ti and generate Ti in matrix grains 2 The Cu reinforcing phase realizes the effect of improving the sinterability and the force of TMCs.
Compared with CNTs with non-uniform reserved microstructures, the CNTs are fully reacted in a sintering mode to generate nano TiC, so that the strength strengthening effect on TMCs is more remarkable; meanwhile, the invention regulates and controls Ti by constructing a coarse-grain and fine-grain bimodal matrix 2 The distribution of Cu and TiC in Ti matrix provides guarantee for preparing high-strength plastic multidirectional heterogeneous TMCs. Specifically, the toughening principle of the invention is as follows: (1) The solid state sintering of the bimodal heterogeneous Cu@CNTs/titanium-based composite powder enables CNTs to generate in-situ thermal synthesis reaction, promotes the generation of intercrystalline nano TiC, and is beneficial to the generation of Ti in the crystal due to the long-distance diffusion of Cu atoms caused by severe thermal effect 2 Cu and Cu jointly block dislocation movement, so that the intensity of TMCs is improved; (2) The built bimodal matrix promotes the accumulation of geometrically necessary dislocations due to the incompatibility of plastic deformation between coarse and fine grains, combined with fine grain regions consisting of inter-and intra-crystalline TiC and Ti 2 The two-stage net structure constructed by Cu can improve the ductility, namely the plasticity, of TMCs. In conclusion, the multiphase heterogeneous titanium-based composite material realizes the matching of high strength and high plasticity.
The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized in that in the first step, the base material is TC6, TC4 or TC11 spherical titanium alloy powder, the particle size of the small-particle-size spherical titanium alloy powder is 15-53 mu m, and the particle size of the large-particle-size spherical titanium alloy powder is 75-150 mu m; the mass purity of the acid-washed carbon nano tube is more than 95%, the tube diameter is 8-15 nm, the length is 50 mu m, the soluble copper ion-containing compound is copper sulfate, copper nitrate or copper acetate, and the mass purity is more than 99.99%.
The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized in that the mass ratio of the acid-washed carbon nano tube to the soluble copper ion-containing compound in the second step is 1-3:1, and the time for uniform ultrasonic dispersion is 20-30 min; the alkaline solution is sodium hydroxide solution or potassium hydroxide solution with the concentration of 0.05 mol/L-0.15 mol/L, and the standing time is 12 h-18 h; the calcination reduction temperature is 200-400 ℃ and the calcination reduction time is 3-5 h; the mass ratio of the Cu@CNTs composite powder to the small-particle-size spherical titanium alloy powder is 0.3-0.7:100, the ball-milling mixing ratio is 3-6:1, the ball-milling rotating speed is 150-250 rpm, and the ball-milling time is 4-6 hours.
The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized in that in the third step, the mass ratio of the heterogeneous Cu@CNTs/titanium-based composite powder to the large-particle-size spherical titanium alloy powder is 0.6-3:13, the ball-material ratio of ball milling and mixing is 3-6:1, the ball milling rotating speed is 50-150 rpm, and the ball milling time is 10-30 min.
The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized in that the sintering and forming temperature of the spark plasma in the fourth step is 900-1100 ℃, the heat preservation time is 3-6 min, and the hot rolling temperature is 800-1000 ℃.
Meanwhile, the invention also discloses a high-strength plastic multiphase heterogeneous titanium-based composite material, which is characterized by being prepared by the method.
Compared with the prior art, the invention has the following advantages:
1. compared with the prior art, the sacrificial CNTs junctionStructural integrity to obtain its direct interface reaction product with Ti x C y As the transition layer to strengthen the infiltration degree of the CNTs-Ti interface and cause the defect of losing the partial strengthening performance of CNTs on the CNTs/Ti composite material, the invention adopts Cu doped CNTs to improve the interface bonding degree of CNTs and Ti-based powder and promote the uniform distribution of CNTs on the surface of Ti-based powder, thereby generating Ti in matrix grains 2 A Cu reinforcing phase; compared with CNTs with non-uniform reserved microstructure, the invention generates TiC reinforcing phase among matrix crystals by fully reacting the CNTs after sintering, and utilizes hybrid Ti 2 Cu and TiC jointly block dislocation movement, so that the intensity of TMCs is improved; compared with a homogeneous Cu@CNTs/Ti composite material, the invention promotes the accumulation of geometrically necessary dislocation by constructing a bimodal matrix and improves the plasticity of TMCs, thereby realizing the high-strength-high-plasticity matching of the titanium-based composite material.
2. Compared with the chemical plating preparation method of the metal nanoparticle modified CNTs in the prior art, the preparation method has the disadvantages of high cost and complicated process, and the phenomenon of serious agglomeration and shedding of the metal nanoparticles on the CNTs, the preparation method takes the pickling CNTs as a carrier, introduces nano defects and functional groups on the surfaces of the CNTs through pickling treatment to enhance hydrophilicity and Cu ion adsorption capacity, regulates and controls the mass ratio of the CNTs to soluble copper ion compounds, and enables Cu ions to be thermally reduced into simple substance Cu particles by hydrogen in an argon-hydrogen mixed atmosphere through simple one-step calcination reduction, thereby loading Cu nanoparticles on the CNTs in situ, improving the uniform dispersity and the tight combination degree of the Cu nanoparticles on the CNTs, being easy to realize the preparation process, being convenient for regulating and controlling the loading capacity of the Cu nanoparticles, and being suitable for industrialized mass production.
3. The invention carries out double peak (coarse crystal and fine crystal) and isomerization (in-situ generation of intercrystalline nano TiC and intracrystalline Ti) on Cu@CNTs/titanium matrix composite material 2 Cu reinforcing phases are distributed at the interface and in the interface) structural design, the reinforcing-toughening effect of the titanium-based composite material is remarkably improved by utilizing bimodal grains and multiphase reinforcement, the room-temperature tensile strength of the obtained multiphase heterogeneous titanium-based composite material is 1160-1506 MPa, the elongation after fracture is 9-12.5%, and the ductility is far higher than that of the prior reported CNTs reinforced Ti-based composite materialMatching level.
The technical scheme of the invention is further described in detail through the drawings and the embodiments.
Drawings
FIG. 1 is a flow chart of a preparation process of the bimodal heterogeneous Cu@CNTs/titanium-based composite powder.
FIG. 2a is a graph showing the microscopic morphology of the Cu@CNTs composite powder prepared in example 1 of the invention.
FIG. 2b is an XRD pattern of the Cu@CNTs composite powder prepared in example 1 of the invention.
FIG. 3 is a microstructure of the heterogeneous Cu@CNTs/TC4 composite powder prepared in example 1 of the invention.
FIG. 4 is a diagram showing the microscopic morphology of the bimodal heterogeneous Cu@CNTs/TC4 composite powder prepared in example 1 of the invention after being sintered and molded by spark plasma.
FIG. 5 is a graph of the microscopic morphology of the heterogeneous Cu@CNTs/TC4 composite material prepared in example 1 of the invention.
FIG. 6 is a diagram showing the microscopic morphology of the heterogeneous Cu@CNTs/TC4 composite powder prepared in comparative example 2 after being sintered and molded by spark plasma.
FIG. 7 is a graph showing engineering stress-strain curves at room temperature of the heterogeneous titanium-based composite materials prepared in examples 1 to 3 according to the present invention, the TC4 material prepared in comparative example 1, and the titanium-based composite material prepared in comparative example 2.
Detailed Description
Example 1
As shown in fig. 1, the present embodiment includes the steps of:
step one, selecting raw materials: spherical TC4 titanium alloy powder with the particle size of 15-53 mu m and spherical TC4 titanium alloy powder with the particle size of 75-150 mu m prepared by a rotating electrode method are respectively selected as matrix materials, and acid-washed carbon nano tubes with the mass purity of more than 95%, the tube diameter of 8-15 nm and the length of 50 mu m and copper sulfate with the mass purity of more than 99.99% are selected as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing 0.8g of the acid-washed carbon nano tube selected in the first step and 0.4g of copper sulfate by ultrasonic waves for 25min, dripping a sodium hydroxide solution with the concentration of 0.1mol/L to be neutral, standing for 15h, drying the obtained nano powder, placing the dried nano powder into a tubular furnace, calcining and reducing the nano powder for 4h at the temperature of 300 ℃ in argon-hydrogen atmosphere, cooling the nano powder to room temperature to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, placing 0.6g of the Cu@CNTs composite powder and 119.4g of spherical TC4 titanium alloy powder with the particle size of 15-53 mu m selected in the first step into a stainless steel ball milling tank, and installing the stainless steel ball milling tank into a planetary ball mill for uniform ball milling and mixing, wherein the ball milling and mixing ball milling speed is 5:1, the ball milling speed is 5 rpm, and the ball milling time is 5h, so as to obtain the isomeric Cu@CNT4 composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing 110g of the heterogeneous Cu@CNTs/TC4 composite powder prepared in the second step and 10g of the spherical TC4 titanium alloy powder with the particle size of 75-150 μm selected in the first step into a planetary ball mill for ball milling and mixing uniformly, wherein the ball milling and mixing uniformly has a ball material ratio of 5:1, the ball milling rotating speed is 100rpm, and the ball milling time is 20min, so as to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/TC4 composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: the bimodal isomerism Cu@CNTs/TC4 composite powder prepared in the third step is placed in a discharge plasma sintering furnace, is kept at 1000 ℃ for 5min, and is subjected to hot rolling at 900 ℃ to obtain a heterogeneous isomerism titanium-based composite material, and the heterogeneous isomerism Cu@CNTs/TC4 composite material is obtained.
The multiphase heterogeneous titanium matrix composite prepared in the embodiment is subjected to room temperature mechanical properties by adopting a universal testing machine, and the result shows that the room temperature tensile strength of the multiphase heterogeneous titanium matrix composite is 1470MPa and the elongation after fracture is 12.34%.
Fig. 2a is a microscopic morphology diagram of the cu@cnts composite powder prepared in this example, and as can be seen from fig. 2a, cu ions are loaded on CNTs in morphology of Cu particles after calcination and reduction.
Fig. 2b is an XRD pattern of the cu@cnts composite powder prepared in this example, and as can be seen from fig. 2b, the corresponding carbon diffraction peak at 2θ=26.31°, the corresponding PDF card being 75-0444; corresponding to the diffraction peaks of elemental copper at 2 theta=43.32 degrees, 50.45 degrees and 74.12 degrees, the corresponding PDF card is 99-0034, which indicates that Cu particles loaded on CNTs in the Cu@CNTs composite powder are elemental Cu.
FIG. 3 is a microscopic morphology diagram of the heterogeneous Cu@CNTs/TC4 composite powder prepared in the embodiment, and as can be seen from FIG. 3, cu@CNTs in the heterogeneous Cu@CNTs/TC4 composite powder are distributed on the surface of spherical TC4 titanium alloy powder with the particle size of 15-53 mu m.
FIG. 4 is a microscopic morphology chart of the bimodal heterogeneous Cu@CNTs/TC4 composite powder prepared in the embodiment after being sintered and molded by spark plasma, and as can be seen from FIG. 4, large-size TC4 grains with the grain diameters of 75-150 μm (no precipitated phase generation at grain boundaries) and small-size TC4 grains with the grain diameters of 15-53 μm (precipitated phase generation at grain boundaries and net-shaped distribution of the precipitated phases) are distributed in the sintered and molded composite material, namely the bimodal heterogeneous characteristic is achieved.
FIG. 5 is a microstructure of the heterogeneous Cu@CNTs/TC4 composite material prepared in the embodiment, and as can be seen from FIG. 5, the microstructure of the heterogeneous Cu@CNTs/TC4 composite material is obviously refined, but the bimodal isomerism characteristics are not changed.
Comparative example 1
This comparative example differs from example 1 in that: the process of ball milling to prepare the heterogeneous Cu@CNTs/TC4 composite powder in the second step and the process of ball milling to prepare the bimodal heterogeneous titanium-based composite powder in the third step are omitted, and the spherical TC4 titanium alloy powder with the particle size of 15-53 μm is directly subjected to the process in the fourth step to obtain the TC4 material.
The TC4 material prepared in the comparative example is subjected to room temperature mechanical properties by adopting a universal testing machine, and the result shows that the room temperature tensile strength of the TC4 material is 1194MPa and the elongation after fracture is 8.34%.
Comparative example 2
This comparative example differs from example 1 in that: the process of ball milling to prepare the bimodal heterogeneous titanium-based composite powder in the third step is omitted, and the heterogeneous Cu@CNTs/TC4 composite powder prepared in the second step is directly subjected to the process in the fourth step to obtain the titanium-based composite material.
Fig. 6 is a microscopic morphology diagram of the heterogeneous cu@cnts/TC4 composite powder prepared in this comparative example after sintering and forming by spark plasma, and it can be seen from fig. 6 that nano TiC and homogeneous TC4 grains distributed in a network form are generated in situ at the grain boundary in the sintered and formed composite material.
The titanium-based composite material prepared in the comparative example is subjected to room temperature mechanical properties by adopting a universal testing machine, and the result shows that the room temperature tensile strength of the titanium-based composite material is 1534MPa and the elongation after fracture is 7.1%.
Comparing fig. 4 of example 1 with fig. 6 of comparative example 2, it can be seen that the present invention utilizes titanium alloy powders with different particle diameters to construct a bimodal matrix, thereby realizing the matching of high strength and high plasticity of the titanium matrix composite material.
Example 2
As shown in fig. 1, the present embodiment includes the steps of:
step one, selecting raw materials: spherical TC4 titanium alloy powder with the particle size of 15-53 mu m and spherical TC4 titanium alloy powder with the particle size of 75-150 mu m prepared by a rotating electrode method are respectively selected as matrix materials, and acid-washed carbon nano tubes with the mass purity of more than 95%, the tube diameter of 8-15 nm and the length of 50 mu m and copper sulfate with the mass purity of more than 99.99% are selected as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing 0.8g of the acid-washed carbon nano tube selected in the first step and 0.4g of sulfuric acid by ultrasonic for 25min, dripping a sodium hydroxide solution with the concentration of 0.1mol/L to be neutral, standing for 15h, drying the obtained nano powder, placing the dried nano powder into a tubular furnace, calcining and reducing for 4h at 300 ℃ in argon-hydrogen atmosphere, cooling to room temperature to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, placing 0.6g of Cu@CNTs composite powder and 119.4g of spherical TC4 titanium alloy powder with the particle size of 15-53 mu m selected in the first step into a stainless steel ball milling tank, and installing the stainless steel ball milling tank into a planetary ball mill for uniform ball milling and mixing, wherein the ball milling and mixing ball milling speed is 5:1, the ball milling time is 5h, and marking the copper-doped carbon nano tube composite powder as the isomeric Cu@CNTs/TC4 composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing 115g of the heterogeneous Cu@CNTs/TC4 composite powder prepared in the second step and 5g of the spherical TC4 titanium alloy powder with the particle size of 75-150 μm selected in the first step into a planetary ball mill for ball milling and mixing uniformly, wherein the ball milling and mixing uniformly has a ball material ratio of 5:1, the ball milling rotating speed is 100rpm, and the ball milling time is 20min, so as to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/TC4 composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: the bimodal isomerism Cu@CNTs/TC4 composite powder prepared in the third step is placed in a discharge plasma sintering furnace, is kept at 1000 ℃ for 5min, and is subjected to hot rolling at 900 ℃ to obtain a heterogeneous isomerism titanium-based composite material, and the heterogeneous isomerism Cu@CNTs/TC4 composite material is obtained.
The multiphase heterogeneous titanium matrix composite prepared in the embodiment is subjected to room temperature mechanical properties by adopting a universal testing machine, and the result shows that the room temperature tensile strength of the multiphase heterogeneous titanium matrix composite is 1483MPa and the elongation after fracture is 9.74%.
Example 3
As shown in fig. 1, the present embodiment includes the steps of:
step one, selecting raw materials: spherical TC4 titanium alloy powder with the particle size of 15-53 mu m and spherical TC4 titanium alloy powder with the particle size of 75-150 mu m prepared by a rotating electrode method are respectively selected as matrix materials, and acid-washed carbon nano tubes with the mass purity of more than 95%, the tube diameter of 8-15 nm and the length of 50 mu m and copper sulfate with the mass purity of more than 99.99% are selected as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing 0.8g of the acid-washed carbon nano tube selected in the first step and 0.4g of copper sulfate by ultrasonic waves for 25min, dripping a sodium hydroxide solution with the concentration of 0.1mol/L to be neutral, standing for 15h, drying the obtained nano powder, placing the dried nano powder into a tubular furnace, calcining and reducing the nano powder for 4h at the temperature of 300 ℃ in argon-hydrogen atmosphere, cooling the nano powder to room temperature to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, placing 0.6g of the Cu@CNTs composite powder and 119.4g of spherical TC4 titanium alloy powder with the particle size of 15-53 mu m selected in the first step into a stainless steel ball milling tank, and installing the stainless steel ball milling tank into a planetary ball mill for uniform ball milling and mixing, wherein the ball milling and mixing ball milling speed is 5:1, the ball milling speed is 5 rpm, and the ball milling time is 5h, so as to obtain the isomeric Cu@CNT4 composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing 100g of the heterogeneous Cu@CNTs/TC4 composite powder prepared in the second step and 20g of the spherical TC4 titanium alloy powder with the particle size of 75-150 μm selected in the first step into a planetary ball mill for ball milling and mixing uniformly, wherein the ball milling and mixing uniformly has a ball material ratio of 5:1, the ball milling rotating speed is 100rpm, and the ball milling time is 20min, so as to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/TC4 composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: the bimodal isomerism Cu@CNTs/TC4 composite powder prepared in the third step is placed in a discharge plasma sintering furnace, is kept at 1000 ℃ for 5min, and is subjected to hot rolling at 900 ℃ to obtain a heterogeneous isomerism titanium-based composite material, and the heterogeneous isomerism Cu@CNTs/TC4 composite material is obtained.
The multiphase heterogeneous titanium matrix composite prepared in the embodiment is subjected to room temperature mechanical properties by adopting a universal testing machine, and the result shows that the room temperature tensile strength of the multiphase heterogeneous titanium matrix composite is 1255MPa, and the elongation after fracture is 12.44%.
FIG. 7 is a graph showing the engineering stress-strain at room temperature of the heterogeneous titanium-based composite materials prepared in examples 1 to 3 and TC4 material prepared in comparative example 1, and the engineering stress-strain curve of the heterogeneous titanium-based composite material prepared in comparative example 2, and it can be seen from FIG. 7 that the tensile strength at room temperature and elongation after fracture of the heterogeneous titanium-based composite material prepared in comparative example 2 are improved but the elongation after fracture are reduced, respectively, in comparison with the TC4 material prepared in comparative example 1 to 3, and that the tensile strength at room temperature and elongation after fracture, namely strength and plasticity, of the heterogeneous titanium-based composite materials prepared in examples 1 to 3 are remarkably improved, respectively, by using Cu doped CNTs in examples 1 to 3 and comparative example 2, the formation of inter-crystalline TiC is effectively promoted by interfacial thermal synthesis reaction through sintering, and the long-distance diffusion of Cu atoms due to severe thermal effect contributes to the formation of Ti in crystals 2 Cu, which together hinder dislocation movement, increases TMCs strength, but is more brittle Ti 2 The Cu and TiC reinforcing phases easily cause stress concentration, and the plasticity of TMCs is not optimized, so that the plasticity of the titanium-based composite material prepared in comparative example 2 is reduced; in contrast to comparative example 2, exampleAccording to the preparation method of 1-3, on the basis of adopting Cu doped CNTs, a bimodal matrix is constructed by introducing TC4 coarse grains which are slightly coarser than TC4 fine grains, so that accumulation of geometrically necessary dislocation caused by incompatibility of plastic deformation between the coarse grains and the fine grains is promoted, the plasticity of the composite material is promoted, and under the condition of slightly sacrificing strength (compared with the TC4 material prepared in comparative example 1, the strength of the multiphase heterogeneous titanium-based composite material prepared in example 1 is reduced by 4.2%, but the plasticity is obviously improved by 73.8%), and high strength-high plasticity synergy of TMCs is realized.
Example 4
As shown in fig. 1, the present embodiment includes the steps of:
step one, selecting raw materials: spherical TC6 titanium alloy powder with the particle size of 15-53 mu m and spherical TC6 titanium alloy powder with the particle size of 75-150 mu m prepared by a rotating electrode method are respectively selected as matrix materials, and acid-washed carbon nano tubes with the mass purity of more than 95%, the tube diameter of 8-15 nm and the length of 50 mu m and copper nitrate pentahydrate with the mass purity of more than 99.99% are selected as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing 0.8g of the acid-washed carbon nano tube selected in the first step and 0.8g of copper nitrate pentahydrate by ultrasonic for 20min, dripping a potassium hydroxide solution with the concentration of 0.05mol/L to be neutral, standing for 12h, drying the obtained nano powder, placing the dried nano powder into a tubular furnace, calcining and reducing the nano powder for 3h at 200 ℃ in argon-hydrogen atmosphere, cooling the nano powder to room temperature to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, placing 0.36g of the Cu@CNTs composite powder and 119.64g of spherical TC6 titanium alloy powder with the particle size of 15-53 mu m selected in the first step into a stainless steel ball milling tank, and installing the stainless steel ball milling tank into a planetary ball mill for uniform ball milling and mixing, wherein the ball milling mixing ball milling material ratio is 3:1, the ball milling rotating speed is 150rpm, and the ball milling time is 4h to obtain the isomeric Cu@CNTs composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing 110g of the heterogeneous Cu@CNTs/TC6 composite powder prepared in the second step and 10g of the spherical TC6 titanium alloy powder with the particle size of 75-150 μm selected in the first step into a planetary ball mill for ball milling and mixing uniformly, wherein the ball milling and mixing uniformly has a ball material ratio of 3:1, the ball milling rotating speed is 50rpm, and the ball milling time is 10min, so as to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/TC6 composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: the bimodal isomerism Cu@CNTs/TC6 composite powder prepared in the third step is placed in a discharge plasma sintering furnace, kept at 900 ℃ for 3min, and then subjected to hot rolling at 800 ℃ to obtain a heterogeneous isomerism titanium-based composite material, which is marked as a heterogeneous isomerism Cu@CNTs/TC6 composite material.
The multiphase heterogeneous titanium matrix composite prepared in the embodiment is subjected to room temperature mechanical properties by adopting a universal testing machine, and the result shows that the room temperature tensile strength of the multiphase heterogeneous titanium matrix composite is 1160MPa, and the elongation after fracture is 12.5%.
Example 5
As shown in fig. 1, the present embodiment includes the steps of:
step one, selecting raw materials: spherical TC11 titanium alloy powder with the particle size of 15-53 mu m and spherical TC11 titanium alloy powder with the particle size of 75-150 mu m prepared by a rotating electrode method are respectively selected as matrix materials, and acid-washed carbon nano tubes with the mass purity of more than 95%, the tube diameter of 8-15 nm and the length of 50 mu m and copper acetate with the mass purity of more than 99.99% are selected as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing 0.8g of the acid-washed carbon nano tube selected in the first step and 0.27g of copper acetate by ultrasonic waves for 30min, dripping a potassium hydroxide solution with the concentration of 0.15mol/L to be neutral, standing for 18h, drying the obtained nano powder, placing the dried nano powder into a tubular furnace, calcining and reducing the nano powder for 5h at 400 ℃ in argon-hydrogen atmosphere, cooling the nano powder to room temperature to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, placing 0.84g of Cu@CNTs composite powder and 119.16g of spherical TC11 titanium alloy powder with the particle size of 15-53 mu m selected in the first step into a stainless steel ball milling tank, and installing the stainless steel ball milling tank into a planetary ball mill for uniform ball milling and mixing, wherein the ball milling and mixing ball milling speed is 6:1, and the ball milling time is 6h, thereby obtaining the isomeric Cu@CNTs/TC11 composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing 110g of the heterogeneous Cu@CNTs/TC11 composite powder prepared in the second step and 10g of the spherical TC11 titanium alloy powder with the particle size of 75-150 mu m selected in the first step into a planetary ball mill for ball milling and mixing uniformly, wherein the ball milling and mixing uniformly has a ball material ratio of 6:1, the ball milling rotating speed is 150rpm, and the ball milling time is 30min, so as to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/TC11 composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: the bimodal isomerism Cu@CNTs/TC11 composite powder prepared in the third step is placed in a discharge plasma sintering furnace, kept at 1100 ℃ for 6min, and then subjected to hot rolling at 1000 ℃ to obtain a heterogeneous isomerism titanium-based composite material, which is marked as a heterogeneous isomerism Cu@CNTs/TC11 composite material.
The multiphase heterogeneous titanium matrix composite prepared in the embodiment is subjected to room temperature mechanical properties by adopting a universal tester, and the result shows that the room temperature tensile strength of the multiphase heterogeneous titanium matrix composite is 1506MPa and the elongation after fracture is 9%.
The above description is only of the preferred embodiments of the present invention, and is not intended to limit the present invention. Any simple modification, variation and equivalent variation of the above embodiments according to the technical substance of the invention still fall within the scope of the technical solution of the invention.
Claims (6)
1. The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized by comprising the following steps of:
step one, selecting raw materials: respectively selecting small-particle-size spherical titanium alloy powder and large-particle-size spherical titanium alloy powder prepared by a rotating electrode method as matrix materials, and selecting acid-washed carbon nano tubes and soluble copper ion-containing compounds as reinforcement precursors;
step two, preparing heterogeneous titanium-based composite powder: uniformly dispersing the acid-washed carbon nano tube and the soluble copper ion-containing compound in the first step by ultrasonic, dripping an alkaline solution to adjust the pH value to be neutral, standing, drying the obtained nano powder, calcining and reducing the nano powder in an argon-hydrogen atmosphere to obtain copper-doped carbon nano tube composite powder, marking the copper-doped carbon nano tube composite powder as Cu@CNTs composite powder, and placing the Cu@CNTs composite powder and the small-particle-size spherical titanium alloy powder selected in the first step in a planetary ball mill for ball milling and mixing uniformly to obtain the isomeric titanium-based composite powder which is marked as the isomeric Cu@CNTs/titanium-based composite powder;
step three, preparing bimodal heterogeneous titanium-based composite powder: placing the heterogeneous Cu@CNTs/titanium-based composite powder prepared in the second step and the large-particle-size spherical titanium alloy powder selected in the first step into a planetary ball mill for ball milling and mixing uniformly to obtain bimodal heterogeneous titanium-based composite powder, and marking the bimodal heterogeneous Cu@CNTs/titanium-based composite powder;
step four, preparing a high-strength plastic multiphase heterogeneous titanium-based composite material: carrying out hot rolling on the bimodal isomerism Cu@CNTs/titanium matrix composite powder prepared in the step three after discharge plasma sintering molding to obtain a multiphase isomerism titanium matrix composite material, and marking the multiphase isomerism Cu@CNTs/titanium matrix composite material; the room-temperature tensile strength of the heterogeneous titanium-based composite material is 1160-1506 MPa, and the elongation after fracture is 9-12.5%.
2. The method for preparing the high-strength plastic multiphase heterogeneous titanium-based composite material according to claim 1, wherein in the first step, the base material is TC6, TC4 or TC11 spherical titanium alloy powder, the particle size of the small-particle-size spherical titanium alloy powder is 15-53 microns, and the particle size of the large-particle-size spherical titanium alloy powder is 75-150 microns; the mass purity of the acid-washed carbon nano tube is more than 95%, the tube diameter is 8-15 nm, the length is 50 mu m, the soluble copper ion-containing compound is copper sulfate, copper nitrate or copper acetate, and the mass purity is more than 99.99%.
3. The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material according to claim 1, wherein the mass ratio of the acid-washed carbon nano tube to the soluble copper ion-containing compound in the second step is 1-3:1, and the time for ultrasonic dispersion is 20-30 min; the alkaline solution is sodium hydroxide solution or potassium hydroxide solution with the concentration of 0.05 mol/L-0.15 mol/L, and the standing time is 12 h-18 h; the calcination reduction temperature is 200-400 ℃ and the calcination reduction time is 3-5 h; the mass ratio of the Cu@CNTs composite powder to the small-particle-size spherical titanium alloy powder is 0.3-0.7:100, the ball-milling mixing ratio is 3-6:1, the ball-milling rotating speed is 150-250 rpm, and the ball-milling time is 4-6 hours.
4. The preparation method of the high-strength plastic multiphase heterogeneous titanium-based composite material is characterized in that in the third step, the mass ratio of the heterogeneous Cu@CNTs/titanium-based composite powder to the large-particle-size spherical titanium alloy powder is 0.6-3:13, the ball-milling mixing ratio is 3-6:1, the ball-milling rotating speed is 50 rpm-150 rpm, and the ball-milling time is 10 min-30 min.
5. The method for preparing the high-strength plastic multiphase heterogeneous titanium-based composite material according to claim 1, wherein the sintering and forming temperature of the discharge plasma in the fourth step is 900-1100 ℃, the heat preservation time is 3-6 min, and the hot rolling temperature is 800-1000 ℃.
6. A high strength plastic multiphase heterogeneous titanium-based composite material, characterized in that it is prepared by the method of any one of claims 1-5.
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