CN110747378A - A kind of Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot pressing preparation method thereof - Google Patents
A kind of Ti3AlC2-Al3Ti dual-phase reinforced Al-based composite material and hot pressing preparation method thereof Download PDFInfo
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- 239000002131 composite material Substances 0.000 title claims abstract description 38
- 238000007731 hot pressing Methods 0.000 title claims abstract description 14
- 238000002360 preparation method Methods 0.000 title claims abstract description 8
- 239000000843 powder Substances 0.000 claims abstract description 46
- 238000005245 sintering Methods 0.000 claims abstract description 16
- 239000000919 ceramic Substances 0.000 claims abstract description 13
- 239000002994 raw material Substances 0.000 claims abstract description 12
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 9
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 9
- 239000010439 graphite Substances 0.000 claims abstract description 9
- 229910052582 BN Inorganic materials 0.000 claims abstract description 8
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims abstract description 8
- 239000012300 argon atmosphere Substances 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 239000000463 material Substances 0.000 claims abstract description 6
- 238000000034 method Methods 0.000 claims abstract description 6
- 239000011159 matrix material Substances 0.000 claims description 27
- 238000001816 cooling Methods 0.000 claims description 13
- 239000012856 weighed raw material Substances 0.000 claims description 3
- 238000010952 in-situ formation Methods 0.000 claims description 2
- 238000002156 mixing Methods 0.000 claims description 2
- 229910009818 Ti3AlC2 Inorganic materials 0.000 claims 7
- 238000000498 ball milling Methods 0.000 claims 2
- 238000004321 preservation Methods 0.000 claims 1
- 238000005303 weighing Methods 0.000 claims 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 22
- 238000011065 in-situ storage Methods 0.000 abstract description 9
- 239000002245 particle Substances 0.000 abstract description 7
- 238000001125 extrusion Methods 0.000 abstract 1
- 239000007788 liquid Substances 0.000 abstract 1
- 229910052782 aluminium Inorganic materials 0.000 description 15
- 229910000765 intermetallic Inorganic materials 0.000 description 5
- 230000002787 reinforcement Effects 0.000 description 5
- 238000006243 chemical reaction Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 230000003014 reinforcing effect Effects 0.000 description 3
- 238000005452 bending Methods 0.000 description 2
- 229910010293 ceramic material Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 239000004615 ingredient Substances 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002243 precursor Substances 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000009718 spray deposition Methods 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
- 229910052723 transition metal Inorganic materials 0.000 description 1
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- C22C21/00—Alloys based on aluminium
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- 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
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Abstract
本发明公开一种Ti3AlC2‑Al3Ti双相增强Al基复合材料及其热压制备方法。其原料为Ti3AlC2陶瓷粉和铝粉，其中Ti3AlC2粉的含量为5～40vol.％。把重量比为2:1的玛瑙球和原料粉放入球磨罐中球磨8～10个小时，将配好的原料粉放入涂好氮化硼的石墨模具中，再将石墨模具放入热压烧结炉中，在氩气气氛下进行烧结，烧结温度为700‑900℃，升温速率为5～20℃/min，保温时间为20～60min，在700～900℃下使Ti3AlC2粉和熔融的Al充分反应原位合成Al3Ti；之后待模具随炉冷却到550～650℃，加压20～30MPa，保温保压30～60min，可以使材料致密化而没有Al液挤出。本发明工艺简单，该材料在轻量化方面有重大应用，加入陶瓷颗粒使其具有高强度和良好的耐磨性，原位生成的Al3Ti大大提高了材料的高温性能，可广泛应用于汽车、军工、航空航天等多个领域。
The invention discloses a Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material and a hot pressing preparation method thereof. The raw materials are Ti 3 AlC 2 ceramic powder and aluminum powder, wherein the content of Ti 3 AlC 2 powder is 5-40 vol.%. Put agate balls and raw material powder with a weight ratio of 2:1 into a ball mill for 8 to 10 hours, put the prepared raw material powder into a graphite mold coated with boron nitride, and then put the graphite mold into a hot In a pressure sintering furnace, sintering is carried out in an argon atmosphere, the sintering temperature is 700-900°C, the heating rate is 5-20°C/min, the holding time is 20-60min, and the Ti 3 AlC 2 powder is made at 700-900° C. Fully react with molten Al to synthesize Al 3 Ti in situ; after that, the mold is cooled to 550-650 ℃ with the furnace, pressurized for 20-30 MPa, and kept under pressure for 30-60 minutes, so that the material can be densified without extrusion of Al liquid. The process of the invention is simple, the material has great application in light weight, the addition of ceramic particles makes it have high strength and good wear resistance, the Al 3 Ti generated in situ greatly improves the high temperature performance of the material, and can be widely used in automobiles , military, aerospace and other fields.
Description
技术领域technical field
本发明涉及一种Ti3AlC2-Al3Ti双相增强Al基复合材料及其热压制备方法。The invention relates to a Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material and a hot-pressing preparation method thereof.
背景技术Background technique
铝基复合材料是应现代科学发展需求而涌现出的一种具有强大生命力的材料，具有低密度、较高的强度、模量与塑性、良好的尺寸稳定性、耐磨性和抗疲劳特性以及良好的抗断裂韧性等一系列优点。当前对铝基复合材料的研究主要是以下两个方面：采用连续纤维增强的铝基复合材料，主要应用于航空航天和军事领域；采用不连续增强体增强的铝基复合材料，主要应用于汽车制造业。我国也较为全面地开展了铝基复合材料方向的研究工作，包括纤维增强、颗粒增强、喷射沉积、原位生成和层压复合等方面的研究。取得了一定进展，正走向实用阶段，目前研究的较多的是使用SiC、Al2O3颗粒增强铝基复合材料。但是陶瓷增强铝基复合材料现存的问题是陶瓷脆性难加工、陶瓷与铝界面润湿性差、膨胀系数差异导致微裂纹等。为此，目前也有通过增强体颗粒原位合成，克服外加颗粒增强相与Al基体润湿性不好、存在表面污染等不足。Aluminum matrix composite material is a material with strong vitality that emerged in response to the needs of modern scientific development. It has low density, high strength, modulus and plasticity, good dimensional stability, wear resistance and fatigue resistance. Good fracture toughness and a series of advantages. The current research on aluminum matrix composites is mainly in the following two aspects: aluminum matrix composites reinforced with continuous fibers are mainly used in aerospace and military fields; aluminum matrix composites reinforced with discontinuous reinforcements are mainly used in automobiles manufacturing. my country has also carried out a relatively comprehensive research on aluminum matrix composites, including fiber reinforcement, particle reinforcement, spray deposition, in-situ generation and lamination. Some progress has been made, and it is moving towards the practical stage. At present, most of the research is to use SiC and Al 2 O 3 particles to strengthen aluminum matrix composites. However, the existing problems of ceramic reinforced aluminum matrix composites are that the ceramic is brittle and difficult to process, the wettability of the ceramic and aluminum interface is poor, and the difference in expansion coefficient causes microcracks. For this reason, there are also in-situ synthesis of reinforcing particles to overcome the problems of poor wettability between the reinforcing phase and the Al matrix and surface contamination.
原位合成增强相的种类除了陶瓷外还有金属间化合物，而钛铝系金属间化合物中的Al3Ti由于高熔点、高硬度、高弹性模量及良好的腐蚀性使其成为被广泛应用的高温结构材料。并且Al3Ti的晶格结构和热膨胀系数都与Al相近，这使得其颗粒能与Al基体润湿性较好且界面结合牢固，所以常作为Al基复合材料的理想的颗粒增强相。Besides ceramics, there are also intermetallic compounds, and Al 3 Ti in the titanium-aluminum intermetallic compounds is widely used due to its high melting point, high hardness, high elastic modulus and good corrosion resistance. high temperature structural materials. In addition, the lattice structure and thermal expansion coefficient of Al 3 Ti are similar to those of Al, which makes its particles have good wettability with the Al matrix and strong interface bonding, so it is often used as an ideal particle reinforcement phase for Al-based composites.
若能将高硬度、耐磨损、与Al基体较好润湿性的陶瓷相和具有高温强度、与Al基体热膨胀系数匹配的Al3Ti金属间化合物采用合适的技术原位生成并双相增强Al基复合材料，则将满足Al基复合材料需要的高强度、高耐磨、高韧性、抗热震能力等性能要求。If the ceramic phase with high hardness, wear resistance, and good wettability with Al matrix and Al 3 Ti intermetallic compound with high temperature strength and matching thermal expansion coefficient with Al matrix can be generated in situ by appropriate technology and strengthened by dual phase Al-based composite materials will meet the performance requirements of Al-based composite materials such as high strength, high wear resistance, high toughness, and thermal shock resistance.
Ti3AlC2是一种层状结构的三元碳化物陶瓷材料，属于被称之为MAX相的三元化合物陶瓷材料的一员，M为过渡金属元素，A主要为Ⅲ，Ⅳ主族中的某些元素，X为C或N，n＝1，2，3。与其他Mn+1AXn相化合物相似，Ti3AlC2的原子结合方式兼具共价键、离子键和金属键三种键，因而既有金属的特性，具有较高的导电性、导热性，良好的抗热震性和可加工性；同时又有陶瓷的特性，具有不错的耐磨损、腐蚀性能，良好的抗氧化性、耐高温性，在许多领域具有重要的应用价值。Ti 3 AlC 2 is a ternary carbide ceramic material with a layered structure, which belongs to a member of the ternary compound ceramic material called MAX phase, M is a transition metal element, and A is mainly in the main group III and IV. Some elements of , X is C or N, n=1, 2, 3. Similar to other Mn +1 AX n phase compounds, the atomic bonding of Ti 3 AlC 2 has covalent bonds, ionic bonds and metal bonds, so it has the characteristics of metals and has high electrical conductivity and thermal conductivity. At the same time, it has the characteristics of ceramics, which has good wear resistance, corrosion resistance, good oxidation resistance and high temperature resistance, and has important application value in many fields.
如果能同时得到Ti3AlC2陶瓷和Al3Ti金属间化合物作为增强相来双相增强 Al基复合材料，将使Al基复合材料的强度、耐磨性、耐高温特性等大大提高。但是目前为止，还没有采用Ti3AlC2与Al原位反应得到Ti3AlC2-Al3Ti/Al基复合材料从而达到双相增强效果的报道。If Ti 3 AlC 2 ceramics and Al 3 Ti intermetallic compounds can be simultaneously obtained as reinforcing phases to reinforce Al-based composites in two phases, the strength, wear resistance and high temperature resistance of Al-based composites will be greatly improved. But so far, there is no report on the in-situ reaction of Ti 3 AlC 2 and Al to obtain Ti 3 AlC 2 -Al 3 Ti/Al matrix composites to achieve dual-phase reinforcement.
发明内容SUMMARY OF THE INVENTION
本发明的目的是克服现有铝基复合材料及其制备方法存在的缺点，提供一种原位形成Al3Ti以达到Ti3AlC2-Al3Ti双相增强铝基复合材料及其制备方法。本发明以铝粉和Ti3AlC2粉为前驱体粉，通过粉末冶金技术，获得综合性能优良的铝基复合材料。原位形成的Al3Ti主要来源是在700-900℃温度下Ti3AlC2中解离出来的Ti原子与Al基体发生化学反应。Ti3AlC2与原位形成的Al3Ti在铝基体中分布均匀，同时与铝基体有良好的润湿性，从而形成较强的陶瓷、金属间化合物/金属结合界面，大大提高了铝基复合材料的力学性能和耐磨性。The purpose of the present invention is to overcome the shortcomings of existing aluminum-based composite materials and preparation methods thereof, and to provide an in-situ formation of Al 3 Ti to achieve Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced aluminum-based composite materials and preparation methods thereof . In the invention, aluminum powder and Ti 3 AlC 2 powder are used as precursor powders, and an aluminum matrix composite material with excellent comprehensive performance is obtained through powder metallurgy technology. The main source of Al 3 Ti formed in situ is the chemical reaction between Ti atoms dissociated from Ti 3 AlC 2 and Al matrix at the temperature of 700-900℃. Ti 3 AlC 2 and Al 3 Ti formed in situ are evenly distributed in the aluminum matrix, and at the same time have good wettability with the aluminum matrix, thus forming a strong ceramic, intermetallic compound/metal bonding interface, which greatly improves the aluminum matrix. Mechanical properties and wear resistance of composites.
为达到以上目的，本发明采取的技术方案是：In order to achieve the above purpose, the technical scheme adopted by the present invention is:
1.一种Ti3AlC2-Al3Ti双相增强Al基复合材料，其特征在于：1. a Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material, is characterized in that:
(1)其原料为Ti3AlC2陶瓷粉和Al粉，其中Ti3AlC2粉的含量为5～40vol.％，其余为Al粉；(1) The raw materials are Ti 3 AlC 2 ceramic powder and Al powder, wherein the content of Ti 3 AlC 2 powder is 5-40 vol.%, and the rest is Al powder;
(2)部分Ti3AlC2的Ti原子与Al发生反应，生成Al3Ti，原位形成Ti3AlC2- Al3Ti双相增强Al基复合材料，反应后Al3Ti含量为10.2％～57.6％，Ti3AlC2含量为3.1％～19.3％，其余为Al基体；(2) Part of Ti atoms of Ti 3 AlC 2 react with Al to form Al 3 Ti, and in situ form Ti 3 AlC 2 - Al 3 Ti dual-phase reinforced Al matrix composite material, and the content of Al 3 Ti after the reaction is 10.2%～ 57.6%, Ti 3 AlC 2 content is 3.1% to 19.3%, and the rest is Al matrix;
(3)Ti3AlC2与Al3Ti均匀分布在Al基体中，且与Al基体润湿性良好，界面结合牢固。(3) Ti 3 AlC 2 and Al 3 Ti are uniformly distributed in the Al matrix, and have good wettability with the Al matrix, and the interface is firmly bonded.
2.根据权利1要求所述的一种Ti3AlC2-Al3Ti双相增强Al基复合材料的热压制备方法，其特征在于：该方法包括以下步骤：2. The hot-pressing preparation method of a Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material according to claim 1, characterized in that: the method comprises the following steps:
步骤1，配料：按照一定的比例计算称量Ti3AlC2粉和Al粉，其中Ti3AlC2含量为5～40vol.％，其余为Al粉；Step 1, ingredients: Calculate and weigh Ti 3 AlC 2 powder and Al powder according to a certain proportion, wherein the content of Ti 3 AlC 2 is 5-40 vol.%, and the rest is Al powder;
步骤2，混料：按照2:1的重量比将玛瑙球和称量好的原料粉放入球磨罐中在滚筒球磨机上球磨8～10个小时；Step 2, mixing: put the agate balls and the weighed raw material powder into the ball mill tank according to the weight ratio of 2:1, and ball mill on a roller ball mill for 8 to 10 hours;
步骤3，热压烧结：将配好的原料粉放入涂好氮化硼的石墨模具中，将模具放入热压烧结炉中，在氩气气氛下进行烧结。烧结温度为700～900℃，升温速率为5～20℃/min，保温时间为20～60min；之后让模具随炉冷却到550～650℃，加压20～30MPa，保温保压30～60min以使其致密化；随炉冷却到400℃卸压，降温到80℃之后取出样品，即得到Ti3AlC2-Al3Ti双相增强Al基复合材料。Step 3, hot-pressing sintering: put the prepared raw material powder into a graphite mold coated with boron nitride, put the mold into a hot-pressing sintering furnace, and perform sintering in an argon atmosphere. The sintering temperature is 700~900℃, the heating rate is 5~20℃/min, and the holding time is 20~60min; then the mold is cooled to 550~650℃ with the furnace, and the pressure is 20~30MPa, and the temperature is kept for 30~60min. Make it densified; cool down to 400 ℃ with the furnace to relieve pressure, and take out the sample after cooling to 80 ℃ to obtain the Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al matrix composite material.
本发明所具有的有益效果：The beneficial effects that the present invention has:
由在高温下Ti3AlC2中解离出来的Ti原子与Al基体发生化学反应原为生成了Al3Ti，而剩余的Ti3AlC2保持了原有的形貌，在基体中分布均匀，解决了直接添加陶瓷颗粒所引起的分布不均匀与界面润湿性差的问题。本发明的Ti3AlC2- Al3Ti/Al，其弯曲强度最高可达460MPa，压缩强度最大可达490MPa，维氏硬度最高为2.68GPa，并且在300℃下还能保持380MPa的弯曲强度和430MPa的压缩强度。本发明采用的配料，可采用浇注、粉末冶金等技术，在较宽的温度范围内获得综合性能良好的铝基复合材料。本发明的制备方法具有工艺简单、操作方便、成本低等显著特点，且制备的复合材料在轻量化方面有着重要应用。The chemical reaction between the Ti atoms dissociated from Ti 3 AlC 2 at high temperature and the Al matrix was originally to generate Al 3 Ti, while the remaining Ti 3 AlC 2 maintained the original morphology and was evenly distributed in the matrix. It solves the problems of uneven distribution and poor interface wettability caused by the direct addition of ceramic particles. The Ti 3 AlC 2 - Al 3 Ti/Al of the present invention has a maximum bending strength of 460 MPa, a maximum compressive strength of 490 MPa, a maximum Vickers hardness of 2.68 GPa, and can maintain a bending strength of 380 MPa and a maximum of 380 MPa at 300°C. 430MPa compressive strength. The ingredients used in the present invention can adopt technologies such as casting and powder metallurgy to obtain aluminum-based composite materials with good comprehensive properties in a wide temperature range. The preparation method of the invention has the remarkable characteristics of simple process, convenient operation, low cost, and the like, and the prepared composite material has important application in the aspect of light weight.
本发明的Ti3AlC2-Al3Ti双相增强Al基复合材料具有轻质、高强、高韧、耐磨以及良好的的高温性能，可广泛应用于汽车、军工、航空航天等多个领域。The Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material of the present invention has light weight, high strength, high toughness, wear resistance and good high temperature performance, and can be widely used in automobile, military, aerospace and other fields .
附图说明Description of drawings
图1是Ti3AlC2-Al3Ti双相增强Al基复合材料的扫描电镜照片(SEM)，图2 是Ti3AlC2-Al3Ti双相增强Al基复合材料的XRD图。FIG. 1 is a scanning electron microscope (SEM) photograph of the Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material, and FIG. 2 is an XRD pattern of the Ti 3 AlC 2 -Al 3 Ti dual-phase reinforced Al-based composite material.
具体实施方式Detailed ways
实施方式一Embodiment 1
按照Ti3AlC2粉和Al粉体积比5％比95％，称取铝粉27.702g，Ti3AlC2粉 2.295g，玛瑙球60g放置在球磨罐中，用滚筒球磨机球磨8h，转速90r/min。将配好的原料粉放入涂好氮化硼的石墨模具中，冷压20MPa，将模具放入真空热压炉中，在氩气气氛下进行烧结。烧结温度700℃，升温速率为5℃/min，保温时间为20min；之后让模具随炉冷却到550℃，加压20MPa，保温保压30min以使其致密化；随炉冷却到400℃卸压，降温到80℃之后取出样品，即得到Ti3AlC2- Al3Ti双相增强Al基复合材料。其中，Ti3AlC2含量约3.1％，Al3Ti含量约10.2％，其余为Al。According to the volume ratio of Ti 3 AlC 2 powder and Al powder 5% to 95%, weigh 27.702g of aluminum powder, 2.295g of Ti 3 AlC 2 powder, and 60g of agate balls and place them in a ball mill, and mill them with a roller ball mill for 8h at a speed of 90r/ min. Put the prepared raw material powder into a graphite mold coated with boron nitride, cold-press at 20MPa, put the mold into a vacuum hot-pressing furnace, and sinter in an argon atmosphere. The sintering temperature was 700°C, the heating rate was 5°C/min, and the holding time was 20min; then the mold was cooled to 550°C with the furnace, pressurized at 20MPa, and kept under pressure for 30min to densify it; cooled to 400°C with the furnace to release the pressure , and the sample was taken out after cooling to 80°C to obtain a Ti 3 AlC 2 - Al 3 Ti dual-phase reinforced Al-based composite material. Among them, the content of Ti 3 AlC 2 is about 3.1%, the content of Al 3 Ti is about 10.2%, and the rest is Al.
实施方式二Embodiment 2
按照Ti3AlC2粉和Al粉体积比10％比90％，称取铝粉26.244g，Ti3AlC2粉 4.59g，玛瑙球32g放置在球磨罐中，用滚筒球磨机球磨10h，转速90r/min。将配好的原料粉放入涂好氮化硼的石墨模具中，冷压20MPa，将模具放入真空热压炉中，在氩气气氛下进行烧结。烧结温度760℃，升温速率为10℃/min，保温时间为30min；之后让模具随炉冷却到600℃，加压25MPa，保温保压30min以使其致密化；随炉冷却到400℃卸压，降温到80℃之后取出样品，即得到Ti3AlC2- Al3Ti双相增强Al基复合材料。其中，Ti3AlC2含量约7.8％，Al3Ti含量约25.7％，其余为Al。According to the volume ratio of Ti 3 AlC 2 powder and Al powder of 10% to 90%, weigh 26.244g of aluminum powder, 4.59g of Ti 3 AlC 2 powder, and 32g of agate balls and place them in a ball mill, and mill them with a roller ball mill for 10h at a speed of 90r/ min. Put the prepared raw material powder into a graphite mold coated with boron nitride, cold-press 20MPa, put the mold into a vacuum hot-pressing furnace, and sinter in an argon atmosphere. The sintering temperature was 760°C, the heating rate was 10°C/min, and the holding time was 30min; then the mold was cooled to 600°C with the furnace, pressurized at 25MPa, and kept under pressure for 30min to densify it; the pressure was relieved by cooling to 400°C with the furnace , and the sample was taken out after cooling to 80°C to obtain a Ti 3 AlC 2 - Al 3 Ti dual-phase reinforced Al-based composite material. Among them, the content of Ti 3 AlC 2 is about 7.8%, the content of Al 3 Ti is about 25.7%, and the rest is Al.
实施方式三Embodiment 3
按照Ti3AlC2粉和Al粉体积比20％比80％，称取铝粉23.328g，Ti3AlC2粉 9.18g，玛瑙球65g放置在球磨罐中，用滚筒球磨机球磨10h，转速90r/min。将配好的原料粉放入涂好氮化硼的石墨模具中，冷压20MPa，将模具放入真空热压炉中，在氩气气氛下进行烧结。烧结温度780℃，升温速率为10℃/min，保温时间为30min；之后让模具随炉冷却到620℃，加压25MPa，保温保压30min以使其致密化；随炉冷却到400℃卸压，降温到80℃之后取出样品，即得到Ti3AlC2- Al3Ti双相增强Al基复合材料。其中，Ti3AlC2含量约15.5％，Al3Ti含量约39.8％，其余为Al。According to the volume ratio of Ti 3 AlC 2 powder and
实施方式四Embodiment 4
按照Ti3AlC2粉和Al粉体积比30％比70％，称取铝粉20.412g，Ti3AlC2粉 13.77g，玛瑙球69g放置在球磨罐中，用滚筒球磨机球磨10h，转速90r/min。将配好的原料粉放入涂好氮化硼的石墨模具中，冷压20MPa，将模具放入真空热压炉中，在氩气气氛下进行烧结。烧结温度800℃，升温速率为10℃/min，保温时间为30min；之后让模具随炉冷却到630℃，加压30MPa，保温保压30min以使其致密化；随炉冷却到400℃卸压，降温到80℃之后取出样品，即得到Ti3AlC2- Al3Ti双相增强Al基复合材料。其中，Ti3AlC2含量约11.2％，Al3Ti含量约48.1％，其余为Al。According to the volume ratio of Ti 3 AlC 2 powder and
实施方式五Embodiment 5
按照Ti3AlC2粉和Al粉体积比40％比60％，称取铝粉17.496g，Ti3AlC2粉 18.36g，玛瑙球72g放置在球磨罐中，用滚筒球磨机球磨10h，转速90r/min。将配好的原料粉放入涂好氮化硼的石墨模具中，冷压20MPa，将模具放入真空热压炉中，在氩气气氛下进行烧结。烧结温度900℃，升温速率为20℃/min，保温时间为60min；之后让模具随炉冷却到650℃，加压30MPa，保温保压60min以使其致密化；随炉冷却到400℃卸压，降温到80℃之后取出样品，即得到Ti3AlC2- Al3Ti双相增强Al基复合材料。其中，Ti3AlC2含量约19.3％，Al3Ti含量约57.6％，其余为Al。According to the volume ratio of Ti 3 AlC 2 powder and
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