CN110747378B - Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot-pressing preparation method thereof - Google Patents
Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot-pressing preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
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- 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
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C32/0052—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 carbides
Abstract
The invention discloses a Ti3AlC2‑Al3A Ti biphase reinforced Al-based composite material and a hot-pressing preparation method thereof. The raw material is Ti3AlC2Ceramic powder and aluminum powder, wherein Ti3AlC2The content of the powder is 5-40 vol.%. Placing agate balls and raw material powder in a weight ratio of 2:1 into a ball milling tank for ball milling for 8-10 hours, placing the prepared raw material powder into a graphite mold coated with boron nitride, placing the graphite mold into a hot-pressing sintering furnace, sintering in an argon atmosphere at the temperature of 700 plus materials of 900 ℃, at the temperature rise rate of 5-20 ℃/min and at the temperature preservation time of 20-60 min, and enabling Ti to be subjected to Ti-Ti sintering at the temperature of 700-900 DEG C3AlC2The powder and the molten Al are fully reacted to synthesize Al in situ3Ti; and then cooling the die to 550-650 ℃ along with the furnace, pressurizing at 20-30 MPa, and preserving heat and pressure for 30-60 min, so that the material can be densified without extruding Al liquid. The invention has simple process, the material has important application in light weight, the ceramic particles are added to ensure that the material has high strength and good wear resistance, and Al generated in situ3The Ti greatly improves the high-temperature performance of the material, and can be widely applied to a plurality of fields of automobiles, war industry, aerospace and the like.
Description
Technical Field
The invention relates to a Ti3AlC2-Al3Ti biphase reinforced Al-base composite materialA material and a hot-pressing preparation method thereof.
Background
The aluminum-based composite material is a material which has strong vitality and emerges according to the requirements of modern scientific development, and has a series of advantages of low density, higher strength, modulus and plasticity, good dimensional stability, wear resistance, fatigue resistance, good fracture toughness resistance and the like. The current research on aluminum matrix composite materials is mainly based on the following two aspects: the aluminum-based composite material reinforced by continuous fibers is mainly applied to the fields of aerospace and military; the aluminum-based composite material reinforced by the discontinuous reinforcement is mainly applied to the automobile manufacturing industry. China also develops research work in the direction of aluminum matrix composite materials comprehensively, including research on fiber reinforcement, particle reinforcement, jet deposition, in-situ generation, lamination and compounding and the like. The research is mostly carried out at present by using SiC and Al2O3A particulate reinforced aluminum matrix composite. However, the existing problems of the ceramic reinforced aluminum matrix composite material are that the ceramic is brittle and difficult to process, the wettability of the ceramic and aluminum interface is poor, and microcracks are caused by the difference of expansion coefficients. Therefore, the defects of poor wettability, surface pollution and the like of an additional particle reinforcing phase and an Al matrix are overcome by in-situ synthesis of reinforcing body particles.
The kind of the in-situ synthesized reinforcing phase includes intermetallic compound besides ceramic, and Al in the intermetallic compound of Ti-Al series3Ti is a widely used high temperature structural material due to its high melting point, high hardness, high elastic modulus, and good corrosion properties. And Al3The lattice structure and the thermal expansion coefficient of Ti are both close to those of Al, so that the particles can be well wetted with an Al matrix and firmly bonded at an interface, and the Ti is often used as an ideal particle reinforcing phase of an Al-based composite material.
If a ceramic phase with high hardness, wear resistance and better wettability with an Al matrix can be combined with Al which has high-temperature strength and is matched with the thermal expansion coefficient of the Al matrix3The Ti intermetallic compound is generated in situ by adopting a proper technology and reinforces the Al-based composite material in two phases, so that the high strength, high wear resistance and high strength required by the Al-based composite material can be metToughness, thermal shock resistance and the like.
Ti3AlC2The ceramic material is a ternary carbide ceramic material with a layered structure, belongs to a member of a ternary compound ceramic material called MAX phase, M is a transition metal element, A is mainly some elements in III and IV main groups, X is C or N, and N is 1, 2 and 3. With other Mn+1AXnLike the compound, Ti3AlC2The atomic bonding mode of the composite material has three bonds of covalent bond, ionic bond and metallic bond, so that the composite material has the characteristics of metal, higher electrical conductivity and thermal conductivity, and good thermal shock resistance and processability; meanwhile, the ceramic has the characteristics of ceramic, good wear resistance and corrosion resistance, good oxidation resistance and high temperature resistance, and has important application value in many fields.
If Ti can be obtained simultaneously3AlC2Ceramic and Al3The Ti intermetallic compound is used as a reinforcing phase to double-phase reinforce the Al-based composite material, so that the strength, the wear resistance, the high temperature resistance and the like of the Al-based composite material are greatly improved. However, up to now, Ti has not been used3AlC2Reacting with Al in situ to obtain Ti3AlC2-Al3The Ti/Al based composite material can achieve the double-phase reinforcing effect.
Disclosure of Invention
The invention aims to overcome the defects of the existing aluminum-based composite material and the preparation method thereof, and provides an in-situ formed Al3Ti to obtain Ti3AlC2-Al3A Ti dual-phase reinforced aluminum-based composite material and a preparation method thereof. The invention uses aluminum powder and Ti3AlC2The powder is precursor powder, and the aluminum-based composite material with excellent comprehensive performance is obtained by a powder metallurgy technology. Al formed in situ3The main source of Ti is Ti at the temperature of 700-900 DEG C3AlC2The dissociated Ti atoms chemically react with the Al matrix. Ti3AlC2With Al formed in situ3Ti is uniformly distributed in the aluminum matrix and has good wettability with the aluminum matrix, thereby forming a stronger ceramic, intermetallic compound/metal bonding interface and greatly improving the aluminum matrixMechanical property and wear resistance of the composite material.
In order to achieve the above purposes, the technical scheme adopted by the invention is as follows:
1. ti3AlC2-Al3The Ti biphase reinforced Al-based composite material is characterized in that:
(1) the raw material is Ti3AlC2Ceramic powder and Al powder, wherein Ti3AlC2The content of the powder is 5-40 vol.%, and the balance is Al powder;
(2) part of Ti3AlC2React with Al to produce Al3Ti, in situ formation of Ti3AlC2- Al3Ti biphase reinforced Al-base composite material, reacted Al3Ti content of 10.2-57.6%, Ti3AlC2The content is 3.1-19.3 percent, and the rest is Al matrix;
(3)Ti3AlC2with Al3Ti is uniformly distributed in the Al matrix, and has good wettability with the Al matrix and firm interface bonding.
2. A Ti according to claim 13AlC2-Al3The hot-pressing preparation method of the Ti dual-phase reinforced Al-based composite material is characterized by comprising the following steps of: the method comprises the following steps:
step 1, batching: calculating and weighing Ti according to a certain proportion3AlC2Powder and Al powder, wherein Ti3AlC2The content is 5-40 vol.%, and the balance is Al powder;
step 2, mixing materials: placing the agate balls and the weighed raw material powder into a ball milling tank according to the weight ratio of 2:1, and carrying out ball milling on the agate balls and the weighed raw material powder for 8-10 hours;
step 3, hot-pressing sintering: and (3) putting the prepared raw material powder into a graphite mold coated with boron nitride, putting the mold into a hot-pressing sintering furnace, and sintering in an argon atmosphere. The sintering temperature is 700-900 ℃, the heating rate is 5-20 ℃/min, and the heat preservation time is 20-60 min; then cooling the mold with the furnace to 550-650 ℃, pressurizing to 20-30 MPa, and keeping the temperature and pressure for 30-60 min to densify the mold; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain Ti3AlC2-Al3Ti biphase reinforced Al-based composite material.
The invention has the following beneficial effects:
by Ti at high temperature3AlC2The dissociated Ti atoms chemically react with the Al matrix to form Al3Ti, and the remainder of Ti3AlC2The original appearance is kept, the ceramic particles are uniformly distributed in the matrix, and the problems of nonuniform distribution and poor interface wettability caused by directly adding the ceramic particles are solved. Ti of the invention3AlC2- Al3The bending strength of Ti/Al can reach 460MPa at most, the compression strength can reach 490MPa at most, the Vickers hardness is 2.68GPa at most, and the bending strength of 380MPa and the compression strength of 430MPa can be maintained at 300 ℃. The aluminum-based composite material with good comprehensive performance can be obtained in a wider temperature range by adopting the materials and adopting the technologies of casting, powder metallurgy and the like. The preparation method has the remarkable characteristics of simple process, convenience in operation, low cost and the like, and the prepared composite material has important application in light weight.
Ti of the invention3AlC2-Al3The Ti dual-phase reinforced Al-based composite material has the advantages of light weight, high strength, high toughness, wear resistance and good high-temperature performance, and can be widely applied to a plurality of fields of automobiles, war industry, aerospace and the like.
Drawings
FIG. 1 is Ti3AlC2-Al3Scanning Electron Micrograph (SEM) of Ti dual-phase reinforced Al-based composite material, and FIG. 2 shows Ti3AlC2-Al3XRD pattern of Ti biphase reinforced Al-base composite material.
Detailed Description
Implementation mode one
According to Ti3AlC2The powder and Al powder are 5 to 95 percent in volume ratio, 27.702g of aluminum powder and Ti are weighed3AlC22.295g of powder and 60g of agate balls are placed in a ball milling tank and ball milled for 8 hours by a roller ball mill at the rotating speed of 90 r/min. Placing the prepared raw material powder into a graphite mold coated with boron nitride, cold pressing at 20MPa, and placing the mold into vacuumAnd sintering in an argon atmosphere in a hot pressing furnace. The sintering temperature is 700 ℃, the heating rate is 5 ℃/min, and the heat preservation time is 20 min; then cooling the mold to 550 ℃ along with the furnace, pressurizing to 20MPa, and preserving heat and pressure for 30min to densify the mold; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain the Ti3AlC2- Al3Ti biphase reinforced Al-based composite material. Wherein, Ti3AlC2About 3.1% of Al3Ti content about 10.2%, and the balance Al.
Second embodiment
According to Ti3AlC2The powder and Al powder are mixed in a volume ratio of 10% to 90%, 26.244g of aluminum powder and Ti are weighed3AlC24.59g of powder and 32g of agate balls are placed in a ball milling tank and ball milled for 10 hours by a roller ball mill at the rotating speed of 90 r/min. And (3) putting the prepared raw material powder into a graphite die coated with boron nitride, cold-pressing at 20MPa, putting the die into a vacuum hot-pressing furnace, and sintering under the argon atmosphere. The sintering temperature is 760 ℃, the heating rate is 10 ℃/min, and the heat preservation time is 30 min; then cooling the mould to 600 ℃ along with the furnace, pressurizing to 25MPa, and preserving heat and pressure for 30min to densify the mould; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain the Ti3AlC2- Al3Ti biphase reinforced Al-based composite material. Wherein, Ti3AlC2About 7.8% of Al3Ti content about 25.7%, and the balance Al.
Third embodiment
According to Ti3AlC2The volume ratio of the powder to the Al powder is 20 percent to 80 percent, 23.328g of aluminum powder and Ti are weighed3AlC29.18g of powder and 65g of agate balls are placed in a ball milling tank and ball milled for 10 hours by a roller ball mill at the rotating speed of 90 r/min. And (3) putting the prepared raw material powder into a graphite die coated with boron nitride, cold-pressing at 20MPa, putting the die into a vacuum hot-pressing furnace, and sintering under the argon atmosphere. The sintering temperature is 780 ℃, the heating rate is 10 ℃/min, and the heat preservation time is 30 min; then cooling the mould to 620 ℃ along with the furnace, pressurizing to 25MPa, and preserving heat and pressure for 30min to densify the mould; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain the Ti3AlC2- Al3Ti biphase reinforced Al-based composite material. Wherein, Ti3AlC2About 15.5% of Al3Ti content of about 39.8%, and the balance Al.
Embodiment IV
According to Ti3AlC2The powder and Al powder are mixed in a volume ratio of 30% to 70%, 20.412g of aluminum powder and Ti powder are weighed3AlC213.77g of powder and 69g of agate balls are placed in a ball milling tank and ball milled for 10 hours by a roller ball mill at the rotating speed of 90 r/min. And (3) putting the prepared raw material powder into a graphite die coated with boron nitride, cold-pressing at 20MPa, putting the die into a vacuum hot-pressing furnace, and sintering under the argon atmosphere. The sintering temperature is 800 ℃, the heating rate is 10 ℃/min, and the heat preservation time is 30 min; then cooling the mould to 630 ℃ along with the furnace, pressurizing to 30MPa, and preserving heat and pressure for 30min to densify the mould; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain the Ti3AlC2- Al3Ti biphase reinforced Al-based composite material. Wherein, Ti3AlC2About 11.2% Al3Ti content about 48.1%, and the balance Al.
Fifth embodiment
According to Ti3AlC2The volume ratio of the powder to the Al powder is 40 percent to 60 percent, 17.496g of aluminum powder and Ti are weighed3AlC218.36g of powder and 72g of agate balls are placed in a ball milling tank and ball milled for 10 hours by a roller ball mill at the rotating speed of 90 r/min. And (3) putting the prepared raw material powder into a graphite die coated with boron nitride, cold-pressing at 20MPa, putting the die into a vacuum hot-pressing furnace, and sintering under the argon atmosphere. The sintering temperature is 900 ℃, the heating rate is 20 ℃/min, and the heat preservation time is 60 min; then cooling the mold to 650 ℃ along with the furnace, pressurizing to 30MPa, and preserving heat and pressure for 60min to densify the mold; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain the Ti3AlC2- Al3Ti biphase reinforced Al-based composite material. Wherein, Ti3AlC2About 19.3% of Al3Ti content of about 57.6%, and the balance Al.
Claims (1)
1. Ti3AlC2-Al3The Ti biphase reinforced Al-based composite material is characterized in that:
(1) the raw material is Ti3AlC2Ceramic powder and Al powder, wherein Ti3AlC2The content of the powder is 5-40 vol.%, and the balance is Al powder;
(2) part of Ti3AlC2React with Al to produce Al3Ti, in situ formation of Ti3AlC2-Al3Ti biphase reinforced Al-base composite material, reacted Al3Ti content of 10.2-57.6%, Ti3AlC2The content is 3.1-19.3 percent, and the rest is Al matrix;
(3)Ti3AlC2with Al3Ti is uniformly distributed in the Al matrix, and has good wettability with the Al matrix and firm interface bonding;
(4) the composite material is prepared by a hot-pressing preparation method, which comprises the following steps:
step 1, batching: calculating and weighing Ti according to a certain proportion3AlC2Powder and Al powder, wherein Ti3AlC2The content is 5-40 vol.%, and the balance is Al powder;
step 2, mixing materials: placing the agate balls and the weighed raw material powder into a ball milling tank according to the weight ratio of 2:1, and carrying out ball milling on the agate balls and the weighed raw material powder for 8-10 hours;
step 3, hot-pressing sintering: placing the prepared raw material powder into a graphite mold coated with boron nitride, placing the mold into a hot-pressing sintering furnace, and sintering in an argon atmosphere, wherein the sintering temperature is 700-900 ℃, the heating rate is 5-20 ℃/min, and the heat preservation time is 20-60 min; then cooling the mold with the furnace to 550-650 ℃, pressurizing to 20-30 MPa, and keeping the temperature and pressure for 30-60 min to densify the mold; cooling to 400 ℃ along with the furnace to release the pressure, cooling to 80 ℃ and taking out the sample to obtain the Ti3AlC2-Al3Ti biphase reinforced Al-based composite material.
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| CN111809075B (en) * | 2020-07-03 | 2021-07-06 | 西安石油大学 | Ti coating Ti3AlC2Particle reinforced Al-based internal combustion engine piston connecting rod and manufacturing method thereof |
| CN112775428B (en) * | 2020-12-25 | 2022-03-25 | 北京交通大学 | Ti generated on the surface of a titanium substrate in situ2AlC ceramic layer and preparation method thereof |
| CN115354182A (en) * | 2022-08-29 | 2022-11-18 | 哈尔滨工业大学 | TiAl in-situ growth 3 Texture of the skeleton Ti 3 AlC 2 Preparation method of reinforced aluminum-based composite material |
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| CN103555982A (en) * | 2013-10-29 | 2014-02-05 | 北京交通大学 | Titanium-aluminum-carbon particle-reinforced zinc-aluminum-based composite material and hot-pressing sintering preparation method thereof |
| CN105463224A (en) * | 2015-11-25 | 2016-04-06 | 陕西理工学院 | TiCx-Al2O3-TiAl3/Al base composite material and manufacturing method thereof |
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| CN103555982A (en) * | 2013-10-29 | 2014-02-05 | 北京交通大学 | Titanium-aluminum-carbon particle-reinforced zinc-aluminum-based composite material and hot-pressing sintering preparation method thereof |
| CN103555982B (en) * | 2013-10-29 | 2016-01-13 | 北京交通大学 | A kind of titanium aluminium carbon granule strengthens Zn Al Alloy Matrix Composites and hot pressed sintering preparation method thereof |
| CN105463224A (en) * | 2015-11-25 | 2016-04-06 | 陕西理工学院 | TiCx-Al2O3-TiAl3/Al base composite material and manufacturing method thereof |
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