CN111545726A - A kind of oriented Ti3SiC2 reinforced magnesium matrix composite material cylinder block and preparation method thereof - Google Patents
A kind of oriented Ti3SiC2 reinforced magnesium matrix composite material cylinder block and preparation method thereof Download PDFInfo
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- 239000011777 magnesium Substances 0.000 title claims abstract description 36
- 239000002131 composite material Substances 0.000 title claims abstract description 26
- 239000011159 matrix material Substances 0.000 title claims abstract description 20
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 title claims abstract description 19
- 229910052749 magnesium Inorganic materials 0.000 title claims abstract description 18
- 238000002360 preparation method Methods 0.000 title description 6
- 229910009817 Ti3SiC2 Inorganic materials 0.000 title description 2
- 239000000919 ceramic Substances 0.000 claims abstract description 22
- 229910000861 Mg alloy Inorganic materials 0.000 claims abstract description 21
- 238000004512 die casting Methods 0.000 claims abstract description 5
- 238000001125 extrusion Methods 0.000 claims abstract description 4
- 230000015572 biosynthetic process Effects 0.000 claims 1
- 239000002245 particle Substances 0.000 abstract description 11
- 239000007787 solid Substances 0.000 abstract description 9
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- 238000013016 damping Methods 0.000 description 9
- 238000000034 method Methods 0.000 description 5
- 230000002787 reinforcement Effects 0.000 description 5
- 238000000227 grinding Methods 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910001018 Cast iron Inorganic materials 0.000 description 3
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- 238000000576 coating method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
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- 229910000838 Al alloy Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
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- 230000008569 process Effects 0.000 description 2
- 230000035939 shock Effects 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229920000426 Microplastic Polymers 0.000 description 1
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 239000011195 cermet Substances 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D19/00—Casting in, on, or around objects which form part of the product
- B22D19/08—Casting in, on, or around objects which form part of the product for building-up linings or coverings, e.g. of anti-frictional metal
- B22D19/085—Casting in, on, or around objects which form part of the product for building-up linings or coverings, e.g. of anti-frictional metal of anti-frictional metal
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D18/00—Pressure casting; Vacuum casting
- B22D18/02—Pressure casting making use of mechanical pressure devices, e.g. cast-forging
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
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Abstract
本发明公布了一种定向化Ti3SiC2陶瓷颗粒增强镁基复合材料的气缸体。把预热到60℃的具有耐磨自润滑性能的Ti3SiC2陶瓷粉体加入到高速搅拌的半固态AE44镁合金中，将熔体升温到700℃保温10mins，再次降温到500℃获得半固态坯料。将温度为500℃的坯料置入压力机，采用0.05‑0.5mm/s的速度热反挤压获得管状气缸套毛坯，对其依次进行粗车、粗镗、车工艺外圆、精镗以及精车外圆，粗珩磨、精珩磨以及平台珩磨，得到镁基气缸套成品。将气缸套置于开发的压铸模具中并采用AE44镁合金压铸，获得缸体。本发明的陶瓷增强镁基气缸体具有密度低的特点，如摘要附图，缸套摩擦后表面无犁沟和颗粒脱落现象。
The invention discloses a cylinder block of oriented Ti 3 SiC 2 ceramic particles reinforced magnesium matrix composite material. The Ti 3 SiC 2 ceramic powder with wear-resistant and self-lubricating properties preheated to 60 ℃ was added to the high-speed stirring semi-solid AE44 magnesium alloy, the melt was heated to 700 ℃ and kept for 10 mins, and then cooled to 500 ℃ to obtain a semi-solid. solid billet. The billet with a temperature of 500°C is placed in the press, and the tubular cylinder liner billet is obtained by hot back extrusion at a speed of 0.05-0.5mm/s, which is sequentially subjected to rough turning, rough boring, turning to the outer circle, fine boring and fine machining. The outer circle of the car, rough honing, fine honing and platform honing are used to obtain the finished magnesium-based cylinder liner. The cylinder liner is placed in the developed die-casting mold and die-casted with AE44 magnesium alloy to obtain the cylinder block. The ceramic-reinforced magnesium-based cylinder block of the present invention has the characteristics of low density. As shown in the abstract drawing, the surface of the cylinder liner is free of furrows and particles falling off after friction.
Description
技术领域technical field
本发明涉及一种定向化Ti3SiC2陶瓷增强镁基复合材料气缸体及其制备方法。The invention relates to an oriented Ti 3 SiC 2 ceramic reinforced magnesium-based composite material cylinder block and a preparation method thereof.
背景技术Background technique
镁合金是世界上最轻的金属结构材料，在汽车工业轻量化、低排放的竞争领域中有着重要的应用价值和广泛的发展前景(参考文献：吴文化，中国能源,2007.29[10].)。镁合金的绝对强度较低，尤其是高温性能较差，限制其在发动机部件和传动机构零部件方面的应用，如缸体衬套，轴瓦等。研究表明，追求耐热且具有耐磨特性镁合金的唯一途径是通过复合化(参考文献：Mortensen,A.and J.Llorca,Materials Today,2010.9[6]:P.1-16)。即在镁合金中添加“增强体/功能体”，在利用不同材料组分本征性能的基础上，通过合理地调控界面和组织结构等综合提高材料的性能。镁基复合材料具有比强度高、比模量高、密度小和热稳定性好等一系列优点，同时还兼具有良好的阻尼性能和电磁屏蔽性能，被认为是继铝基复合材料之后又一影响力极强的轻金属复合材料。由于汽车行驶过程中有振动和摩擦的影响，由此，开发具有高比强度、高比刚度和优良阻尼减震降噪性能及耐磨自润滑特性的Mg基复合材料成为了研究热点。Magnesium alloy is the lightest metal structural material in the world, and has important application value and broad development prospects in the competitive field of lightweight and low emission in the automotive industry (Reference: Wu Wenhua, China Energy, 2007.29[10].) . The absolute strength of magnesium alloys is low, especially the high temperature performance is poor, which limits its application in engine components and transmission parts, such as cylinder bushings, bearing bushes, etc. Studies have shown that the only way to pursue heat-resistant and wear-resistant magnesium alloys is through compounding (reference: Mortensen, A. and J. Llorca, Materials Today, 2010.9 [6]: P.1-16). That is, adding "reinforcing body/functional body" to magnesium alloy, on the basis of utilizing the intrinsic properties of different material components, comprehensively improving the performance of the material by rationally controlling the interface and structure. Magnesium matrix composites have a series of advantages such as high specific strength, high specific modulus, low density and good thermal stability, and also have good damping performance and electromagnetic shielding performance. A very influential light metal composite material. Due to the influence of vibration and friction in the driving process of automobiles, the development of Mg-based composites with high specific strength, high specific stiffness, excellent damping and noise reduction performance, and wear-resistant and self-lubricating properties has become a research hotspot.
汽车缸体衬套既要传递作用力又要承受很高的表面速度，这就要求衬套材料既要具有软组分，以获得良好的运行性能，如磨合性、顺应性以及尽可能小的咬和倾向，且不宜被外来杂质所损伤；又要具有硬组分，以获得良好的耐磨性和抗疲劳强度。因此，创造一种软、硬组分晶粒尽可能均匀分布的金相组织，是提高衬套性能的合理途径。为了取代传统缸体里边的铸铁衬套，达到缸体减重的效果。一种方法是在缸体内壁基体表面镀层，如金属铬，来提高耐磨性，但是镀层与基体存在热膨胀系数不一致已造成脱落，同时缸体的寿命取决于镀层的厚度，而镀层厚度是微米级(CN105603266A)；另外一种方法是采用高硅铝制备发动机缸体(参考文献：Arsha,A.G.,et al.,Materials&Design,2015[88]:P.1201-1209)。经过合适工艺的磨削和珩磨,发动机缸体表面裸露的初生Si可以提供良好的耐磨性能。这样，省掉铸铁衬套，也有利于活塞和缸体之间的接触传热，以有利于材料的回收。但研究发现，脆性的Si颗粒容易从基体脱落且容易破碎。同时，由于Al合金中添加了大量的Si，这也不利于缸体的成型(参考文献：Yu,W.,et al.,Journal of Alloys and Compounds,2018[731]:P.444-451)。因此，现在的研究方向是通过表面处理实现缸体壁的耐磨自润滑性能或者寻求衬套代替铸铁衬套。The need for automotive cylinder liners to both transmit forces and withstand high surface velocities requires that the liner material have both a soft component for good running properties such as running-in, compliance, and as little as possible It has a tendency to bite and is not damaged by foreign impurities; it also has a hard component to obtain good wear resistance and fatigue strength. Therefore, creating a metallographic structure in which the grains of the soft and hard components are distributed as uniformly as possible is a reasonable way to improve the performance of the bushing. In order to replace the cast iron bushing in the traditional cylinder block, the weight reduction effect of the cylinder block is achieved. One method is to coat the surface of the base body on the inner wall of the cylinder, such as metal chromium, to improve the wear resistance, but the thermal expansion coefficient of the coating and the base body are inconsistent, which has caused shedding, and the life of the cylinder depends on the thickness of the coating, and the thickness of the coating is micrometers. grade (CN105603266A); another method is to use high silicon aluminum to prepare the engine block (reference: Arsha, A.G., et al., Materials & Design, 2015 [88]: P.1201-1209). After proper grinding and honing, the exposed primary Si on the surface of the engine block can provide good wear resistance. In this way, the cast iron bushing is omitted, and the contact heat transfer between the piston and the cylinder block is also facilitated, so as to facilitate the recovery of materials. However, the study found that the brittle Si particles are easy to fall off from the matrix and break easily. At the same time, due to the addition of a large amount of Si in the Al alloy, it is not conducive to the forming of the cylinder (Reference: Yu, W., et al., Journal of Alloys and Compounds, 2018 [731]: P.444-451) . Therefore, the current research direction is to realize the wear-resistant and self-lubricating properties of the cylinder wall through surface treatment or to seek bushings to replace cast iron bushings.
近年来，Mg作为最轻的结构材料引起广泛的关注。同时，SiC、TiC和Al2O3颗粒、B4C及C纳米管晶须和纤维等被广泛地用作Mg基复合材料增强体(参考文献：Oakley,R.,R.Cochrane,and R.Stevens Key Engineering Materials.1995.Trans Tech Publ.)。其中，研究最为深入的SiC-Mg基复合材料已被美国Textron公司应用到螺旋桨，导弹尾翼和内部加强的气缸中。拉伸实验表明复合材料的失效机制为SiC与Mg基体两者界面脱离形成裂纹并进一步扩展所致。另外，还发现高的热挤压比易导致硬脆的SiC破裂。针对传统的SiC增-镁基复合材料，Saravanan(参考文献：Saravanan,R.and M.Surappa,MaterialsScience and Engineering:A,2000.276[1]:P.108-116)发现复合材料中30％vol SiC-Mg的耐磨性相比纯镁提高了两个数量级，但硬脆的SiC陶瓷颗粒易从Mg基体脱落造成基体表面严重的“犁沟”划伤。同时，本身不具备阻尼容量的硬脆SiC增强体也不利于复合材料整体的阻尼减震。鉴于此，Das等(参考文献：Das,A.and S.P.Harimkar,Journal of MaterialsScience&Technology,2014.30[11]:P.1059-1070.)通过引入具有高阻尼容量和自润滑性能的碳材料制备SiC-Graphene增强的Mg复合材料来克服此现象。然而，起自润滑和提高阻尼容量作用的石墨在高于350℃氧化环境下很容易氧化失效。由此可见，传统的镁基复合材料增强体存在以下缺点：①本身塑韧性和损伤容限低，②与Mg基体形成的界面结合力不强，硬脆颗粒易脱落导致Mg基体划伤，引入克服此现象的碳材料又容易高温氧化失效，③后期加工易诱发硬脆颗粒破碎，如热挤压。In recent years, Mg has attracted extensive attention as the lightest structural material. Meanwhile, SiC, TiC and Al 2 O 3 particles, B 4 C and C nanotube whiskers and fibers are widely used as Mg-based composite reinforcements (References: Oakley, R., R. Cochrane, and R. .Stevens Key Engineering Materials. 1995. Trans Tech Publish.). Among them, the most deeply researched SiC-Mg matrix composites have been applied to propellers, missile tails and internally reinforced cylinders by American Textron Company. Tensile experiments show that the failure mechanism of the composites is caused by the detachment of the interface between the SiC and the Mg matrix to form cracks and further expansion. In addition, it is also found that high hot extrusion ratio easily leads to cracking of hard and brittle SiC. For traditional SiC-Mg-based composites, Saravanan (Reference: Saravanan, R.and M.Surappa, Materials Science and Engineering: A, 2000.276[1]:P.108-116) found that 30%vol SiC in the composites -The wear resistance of Mg is improved by two orders of magnitude compared with pure magnesium, but the hard and brittle SiC ceramic particles are easy to fall off from the Mg matrix, resulting in serious "furrow" scratches on the surface of the matrix. At the same time, the hard and brittle SiC reinforcement that does not have damping capacity itself is not conducive to the overall damping and shock absorption of the composite material. In view of this, Das et al. (Reference: Das, A. and SP Harimkar, Journal of Materials Science & Technology, 2014. 30 [11]: P. 1059-1070.) prepared SiC-Graphene reinforcement by introducing carbon materials with high damping capacity and self-lubricating properties Mg composites to overcome this phenomenon. However, graphite, which plays the role of self-lubricating and improving damping capacity, is prone to oxidative failure in an oxidizing environment above 350 °C. It can be seen that the traditional magnesium matrix composite reinforcement has the following shortcomings: (1) its own plastic toughness and damage tolerance are low, (2) the interface bonding force formed with the Mg matrix is not strong, and the hard and brittle particles are easy to fall off, causing the Mg matrix to be scratched. Carbon materials that overcome this phenomenon are prone to high temperature oxidation failure, and ③ later processing can easily induce hard and brittle particles to break, such as hot extrusion.
Ti3SiC2等可进行机械加工的新型三元层状金属陶瓷MAX材料，与Mg同属六方晶系具备类似于石墨的层状结构，(参考文献：N.V.Tzenov和M.W.Barsoum,J.Am.Ceram.Soc.,2000,83[4]:825)Ti3SiC2与低碳钢在20m/s和0.8MPa干摩擦条件下对摩，其摩擦系数和摩擦率仅为0.27和1.37×10-6mm3/(N·m)(参考文献：H-X Zhai，et al,Mater.Sci.Forum,2005[475-479]:1251)结构决定性能，⊥c轴的层与层之间在剪切力的作用下容易发生滑动，并发生类似金属的弯折带塑形变形。针对此现象，Barsoum课题组(参考文献：Barsoum,M.,etal.,Nature Materials,2003,[2]:P.107-111)提出了MAX材料的扭折非线弹性变形机制，这与Mg、Ti等密排六方结构的金属的微塑变形机制(Incipent kink bands)类似，由此MAX具备优良的阻尼性能。由此，MAX具备优良的阻尼性能。从而，MAX材料可成为制备具有高阻尼减震和耐磨自润滑特性的镁金属结构材料理想增强体，并可以制备成陶瓷颗粒增强Mg基复合材料的汽车气缸套。因此，本发明采用Ti3SiC2MAX相材料制备Mg基复合材料的汽车气缸套。New ternary layered cermet MAX materials such as Ti 3 SiC 2 that can be machined, belong to the same hexagonal crystal system as Mg and have a layered structure similar to graphite, (References: NVTzenov and MWBarsoum, J.Am.Ceram.Soc .,2000,83[4]:825) Ti 3 SiC 2 and low carbon steel rubbed against low carbon steel under dry friction conditions of 20m/s and 0.8MPa, and the friction coefficient and friction rate were only 0.27 and 1.37×10 -6 mm 3 /(N m) (Reference: HX Zhai, et al, Mater.Sci.Forum, 2005[475-479]:1251) The structure determines the performance, the effect of the shear force between the layers of the ⊥c axis It is easy to slip under the bottom, and the plastic deformation of the metal-like bending belt occurs. In response to this phenomenon, Barsoum's research group (Reference: Barsoum, M., et al., Nature Materials, 2003, [2]: P.107-111) proposed the kink nonlinear elastic deformation mechanism of MAX materials, which is similar to Mg The microplastic deformation mechanism (Incipent kink bands) of metals with close-packed hexagonal structures such as , Ti and so on is similar, so MAX has excellent damping performance. As a result, MAX has excellent damping performance. Therefore, the MAX material can be an ideal reinforcement for the preparation of magnesium metal structural materials with high damping, shock absorption, wear resistance and self-lubricating properties, and can be prepared into a ceramic particle reinforced Mg matrix composite material for automobile cylinder liners. Therefore, the present invention adopts the Ti 3 SiC 2 MAX phase material to prepare the automobile cylinder liner of the Mg-based composite material.
发明内容SUMMARY OF THE INVENTION
本发明的目的在于提供一种定向化Ti3SiC2陶瓷增强镁基复合材料气缸体及其制备方法，其成分如下：The object of the present invention is to provide a kind of oriented Ti 3 SiC 2 ceramic reinforced magnesium matrix composite material cylinder block and its preparation method, and its components are as follows:
缸套中Ti3SiC2陶瓷相的体积含量为5-35vol％，其余为AE44镁合金，缸体其余部分为AE44镁合金。 The volume content of the Ti3SiC2 ceramic phase in the cylinder liner is 5-35 vol%, the rest is AE44 magnesium alloy, and the rest of the cylinder block is AE44 magnesium alloy.
其显微结构如下：Its microstructure is as follows:
缸套中的Ti3SiC2陶瓷相定向分布在AE44镁合金中，其中陶瓷相颗粒分布在镁基体晶界处，二者界面结合牢固。而且，该气缸套可以进行后期的机加工。The Ti 3 SiC 2 ceramic phase in the cylinder liner is oriented and distributed in the AE44 magnesium alloy, and the ceramic phase particles are distributed at the grain boundary of the magnesium matrix, and the interface between the two is firmly bonded. Moreover, the cylinder liner can be machined later.
本发明的定向化Ti3SiC2陶瓷增强镁基复合材料气缸体制备方法，该方法包括以下各步骤：The preparation method of the oriented Ti 3 SiC 2 ceramic reinforced magnesium matrix composite material cylinder block of the present invention comprises the following steps:
步骤1，将Mg合金熔化再降温至半固态，把预热到60℃的Ti3SiC2陶瓷粉体加入到高速搅拌的半固态AE44镁合金熔体中。将熔体升温到700℃保温10mins，再次降温到500℃获得半固态坯料。Step 1, the Mg alloy is melted and then cooled to a semi-solid state, and the Ti 3 SiC 2 ceramic powder preheated to 60° C. is added to the high-speed stirring semi-solid AE44 magnesium alloy melt. The melt was heated to 700 °C for 10 mins, and then cooled to 500 °C to obtain a semi-solid billet.
步骤2，将温度为500℃的坯料置入压力机，使用热反挤压模具，采用0.05-0.5mm/s的速度将坯料推入磨具，获得管状的气缸套毛坯。Step 2, put the blank with a temperature of 500°C into a press, use a hot back extrusion die, and push the blank into the grinding tool at a speed of 0.05-0.5mm/s to obtain a tubular cylinder liner blank.
步骤3，得到的Mg基复合材料气缸套毛坯依次进行粗车、粗镗、车工艺外圆、精镗以及精车外圆，粗珩磨、精珩磨以及平台珩磨，得到镁基缸套成品。In step 3, the obtained Mg-based composite cylinder liner blanks are sequentially subjected to rough turning, rough boring, turning process outer circle, fine boring and fine turning outer circle, rough honing, fine honing and platform honing to obtain a finished magnesium-based cylinder liner.
步骤4，将获得的缸套置于改进的压铸模具中，将融化的AE44镁合金压入到模具中，获得缸体。In step 4, the obtained cylinder liner is placed in an improved die-casting mold, and the molten AE44 magnesium alloy is pressed into the mold to obtain a cylinder block.
本发明的效果：本发明的定向化Ti3SiC2陶瓷增强镁基复合材料气缸体具有密度小和耐磨自润滑特性，其中耐磨自润滑的特性来自于的强韧性Ti3SiC2陶瓷颗粒的定向化，这可以提高发动机缸体的寿命和降低发动机能源消耗，减少排放污染，Effects of the present invention: The oriented Ti 3 SiC 2 ceramic reinforced magnesium-based composite material cylinder block of the present invention has low density and wear-resisting self-lubricating properties, wherein the wear-resisting and self-lubricating properties come from the strong and tough Ti 3 SiC 2 ceramic particles The orientation of the engine, which can improve the life of the engine block and reduce the energy consumption of the engine, reduce emission pollution,
附图说明Description of drawings
图1是Ti3SiC2增强镁基复合材料气缸套微观组织光镜图。Figure 1 is an optical microscope image of the microstructure of the Ti 3 SiC 2 reinforced magnesium matrix composite cylinder liner.
图2是15vol％Ti3SiC2增强镁基复合材料0.5m/s和2MPa压力下与铝合金摩擦副的摩擦表面电镜图。Figure 2 is a tribosurface electron microscope image of a 15vol% Ti 3 SiC 2 reinforced magnesium matrix composite with an aluminum alloy friction pair at a pressure of 0.5 m/s and 2 MPa.
具体实施方式Detailed ways
本发明提供了一种可定向化Ti3SiC2陶瓷增强镁基复合材料气缸套材料及其制备方法，以下结合附图和实施例对本发明进行详细地说明，但本发明并不限于此。The present invention provides an orientable Ti 3 SiC 2 ceramic reinforced magnesium matrix composite cylinder liner material and a preparation method thereof. The present invention is described in detail below with reference to the accompanying drawings and examples, but the present invention is not limited thereto.
实施例1Example 1
在CO2保护气氛下，将AE44镁合金熔化再降温至半固态，把15％vol的Ti3SiC2MAX陶瓷粉体(颗粒粒径为1-20μm)加入到高速搅拌的半固态AE44镁合金熔体中。将其浇铸到开发出的衬套不锈钢磨具中并保压50-100MPa冷却至室温，将熔体升温到700℃保温10mins，再次降温到500℃获得半固态坯料。将温度为500℃的坯料置入压力机，热反挤压制备气缸套，采用1mm/s的速度将坯料推入磨具，获得管状的Ti3SiC2陶瓷基增强AE44镁基气缸套毛坯。如图1所示，微观组织表明陶瓷相Ti3SiC2与金属相Mg基合金各自呈三维空间连续分布，其中陶瓷相Ti3SiC2颗粒分布在Mg基体晶界处，二者界面结合牢固。将获得的缸套置于改进的压铸模具中，将融化的AE44镁合金压入到模具中，获得缸体。Under the protective atmosphere of CO 2 , the AE44 magnesium alloy was melted and then cooled to a semi-solid state, and 15% vol of Ti 3 SiC 2 MAX ceramic powder (particle size of 1-20 μm) was added to the high-speed stirring semi-solid AE44 magnesium alloy in the melt. Cast it into the developed liner stainless steel grinding tool and keep the pressure at 50-100MPa and cool it to room temperature, heat the melt to 700℃ for 10mins, and cool it down to 500℃ again to obtain a semi-solid billet. The billet with a temperature of 500°C was placed in a press, and the cylinder liner was prepared by hot back extrusion. The billet was pushed into the grinding tool at a speed of 1 mm/s to obtain a tubular Ti 3 SiC 2 ceramic-based reinforced AE44 magnesium-based cylinder liner blank. As shown in Figure 1, the microstructure shows that the ceramic phase Ti 3 SiC 2 and the metal phase Mg-based alloy are distributed continuously in three-dimensional space, and the ceramic phase Ti 3 SiC 2 particles are distributed at the grain boundary of the Mg matrix, and the interface between the two is firmly bonded. The obtained cylinder liner was placed in a modified die-casting mold, and the molten AE44 magnesium alloy was pressed into the mold to obtain a cylinder block.
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