WO2021120636A1 - 3D打印制备碳纤维增强SiC陶瓷基复合材料的方法 - Google Patents

3D打印制备碳纤维增强SiC陶瓷基复合材料的方法 Download PDF

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WO2021120636A1
WO2021120636A1 PCT/CN2020/106966 CN2020106966W WO2021120636A1 WO 2021120636 A1 WO2021120636 A1 WO 2021120636A1 CN 2020106966 W CN2020106966 W CN 2020106966W WO 2021120636 A1 WO2021120636 A1 WO 2021120636A1
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carbon fiber
sic
powder
ceramic matrix
fiber reinforced
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French (fr)
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李晨辉
邹阳
史玉升
胡梁
刘江安
吴甲民
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华中科技大学
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Definitions

  • the invention belongs to the field of composite materials, and more specifically, relates to a method for preparing carbon fiber reinforced SiC ceramic matrix composite materials by 3D printing.
  • SiC ceramic matrix composites are expected to be successfully applied in the above-mentioned fields due to their excellent properties such as low density, high thermal conductivity, ablation resistance and abrasion resistance.
  • SiC ceramics have high brittleness and high crack sensitivity, and their inherent difficult-to-process characteristics restrict this material from being formed into complex structural parts, which greatly limits its application range.
  • traditional processing methods have the problems of complex technology and high cost.
  • the blank is obtained by molding or cold isostatic pressing, and then processed into the required shape with the help of CNC machine tools (CNC).
  • CNC machine tools CNC machine tools
  • the forming process depends heavily on the processing ability of CNC.
  • CNC CNC machine tools
  • the processing cost of the components of the honeycomb structure is high, and sometimes it is even difficult to meet the design requirements.
  • ceramic wet molding techniques including grouting, gel injection molding, and direct solidification molding, which are more commonly used in recent years, can be used to prepare complex structures, these methods require the help of molds, which is costly for small batch production. High, not suitable for personalized customization.
  • the ceramic wet molding technology requires the preparation of a slurry with high solid content and good fluidity. The actual solid content of the slurry is difficult to exceed 70wt%. Therefore, the solidification, degreasing and sintering stages of the green body are difficult to avoid. The degree of shrinkage, the geometric accuracy of the sample is relatively low.
  • Additive manufacturing is listed as an advanced manufacturing technology that needs to be developed to enhance national competitiveness and meet future challenges.
  • SLS Selective Laser Sintering
  • 3D printing (additive manufacturing) technologies SLS technology is suitable for rapid manufacturing of parts with complex structures and special shapes, and can meet the rapid prototyping manufacturing requirements of various ceramic parts such as whole and split parts; and SLS technology There is no need to set up a supporting structure during the forming process, which simplifies the post-processing procedures of the formed part, which is expected to solve the difficult problems faced by the preparation of complex structure SiC ceramic matrix composite parts.
  • CN200510020015.5 discloses a method for preparing laser sintering rapid SiC ceramics, which uses laser sintering technology to form SiC preforms and then melt them. Infiltrated silicon and treated with alkali solution to obtain complex-shaped SiC ceramics, but the SiC powder used in this method needs to be sprayed and granulated to ensure good fluidity, which makes the cost of raw materials required for this method high and the preparation process cumbersome.
  • the PF/chopped carbon fiber-Si (phenolic resin coated carbon fiber-Si composite powder) used in the method is prepared by the solvent evaporation method, which also faces the problems of high raw material cost and cumbersome preparation process And because it uses chopped carbon fiber and a small amount of Si powder to form the green body, the powder has low bulk density and poor fluidity, and it is difficult to avoid the problems of poor geometric accuracy of the formed body and large dimensional shrinkage during the carbonization process.
  • the present invention provides a method for preparing carbon fiber reinforced SiC ceramic matrix composites by 3D printing, wherein the method is performed by impregnating a carbonized green body with an organic carbon precursor solution.
  • the secondary carbonization treatment can use the carbon precursor to solidify the residual phase after pyrolysis, increase the strength of the green body to facilitate subsequent operations, and effectively improve the effect of reinforcing and toughening chopped carbon fibers.
  • it can also use the space network formed after carbonization and cracking.
  • the fine secondary carbon refines the pores in the body to prepare carbon fiber reinforced SiC ceramic matrix composites with excellent flexural strength and fracture toughness. Therefore, it is especially suitable for hypersonic aircraft thermal protection systems, hot end parts of aero engines, and high performance Manufacturing of components such as brake systems and space telescope mirror blanks.
  • the present invention proposes a method for preparing carbon fiber reinforced SiC ceramic matrix composite by 3D printing.
  • the method includes the following steps:
  • the specific situation of the particle size distribution in the SiC powder is: the powder with a particle size of 0.1-2 ⁇ m accounts for 0-5wt% of the total SiC powder, and the particle size is 2-40 ⁇ m.
  • SiC powder accounts for 22-55wt% of all SiC powders, and powders with a particle size of 40-250 ⁇ m account for 42-75wt% of all SiC powders.
  • the diameter of the chopped carbon fiber is 0.1-20 ⁇ m
  • the aspect ratio is 5 to 500
  • the addition amount of the chopped carbon fiber accounts for 1-20 wt of the total SiC powder. %.
  • the binder is one or more of epoxy resin, phenolic resin or nylon 12, and the added amount is 3-20 wt% of the SiC powder.
  • the specific method for laser selective sintering is: using manual or mechanical method to spread the powder, and then based on the slice data obtained from the three-dimensional model of the target molded body, using the laser to irradiate layer by layer The SiC/chopped carbon fiber green body is obtained in a specific area of the powder bed.
  • the organic carbon precursor solution is one or more of epoxy resin solution, phenol resin solution or asphalt solution.
  • step (c) the specific process of the carbonization treatment or the secondary carbonization treatment is: placing the sample to be carbonized in a non-oxidizing atmosphere, and heating the binder or carbon precursor Slowly increase the temperature within the solution temperature range, and then quickly increase the temperature to the target temperature of 850°C ⁇ 1100°C and keep it for 1.0h ⁇ 6h for carbonization.
  • step (d) the specific process of the liquid phase silicon infiltration method is: embedding SiC/chopped carbon fiber/carbon blank in metal Si, and then heating to 1420°C under vacuum conditions.
  • the target temperature is 1800°C and the temperature is kept for 0.25h ⁇ 3h.
  • a carbon fiber reinforced SiC ceramic matrix composite material prepared by the above method is provided.
  • the present invention uses an organic carbon precursor solution to infiltrate the carbonized green body, and then heat it to perform secondary carbonization treatment, which can not only use the carbon precursor to solidify the residual phase after pyrolysis, and enlarge the green body
  • the strength is convenient for subsequent operations, and the secondary carbon generated by its pyrolysis can be attached to the surface of the matrix material in the pores as a "carbon consumption layer" to reduce the damage of the molten Si to the matrix chopped carbon fiber, which is beneficial to the toughening effect of the chopped carbon fiber
  • the spatial network of secondary carbon formed after carbonization and cracking of the carbon precursor can further refine and divide the micron-scale pores in the green body into many nano-scale pores, and realize the separation of large-size residual Si in the composite material into sub-micron or The effect of nano-scale Si particles can further enhance the mechanical properties of composite materials;
  • the present invention can effectively optimize the accumulation behavior of the mixed powder by optimizing the particle size distribution of the SiC powder, and compensate for the adverse effect of the addition of chopped carbon fiber on the fluidity of the mixed powder, thereby ensuring the mixed powder It has good fluidity and large bulk density, so only simple mechanical mixing is needed to ensure that the mixed powder has good flow properties and SLS formability, omitting the preparation of raw material powder in the current ceramic SLS rapid prototyping process The required dissolution precipitation method or solvent evaporation method and other cumbersome processes, thereby greatly reducing the preparation cost;
  • the present invention optimizes the process and process parameters for preparing carbon fiber reinforced SiC ceramic matrix composites by 3D printing. Under the combined action of the process parameters, the relative density is greater than 98%, the flexural strength is greater than 180MPa, and the fracture Carbon fiber reinforced SiC ceramic matrix composite material with toughness greater than 2.5MPa ⁇ m 0.5.
  • Fig. 1 is a process flow diagram of 3D printing preparation of carbon fiber reinforced SiC ceramic matrix composite material provided by the present invention
  • FIG. 2 is a schematic diagram of the phase composition distribution of a carbon fiber reinforced SiC ceramic matrix composite prepared by a preferred embodiment of the present invention
  • Example 3 is a photomicrostructure of a green SiC/chopped carbon fiber body containing 6 wt% of chopped carbon fibers prepared in Example 6 of the present invention
  • Example 4 is a photo of the microstructure of a corrosion section of a carbon fiber reinforced SiC ceramic matrix composite material containing 6 wt% chopped carbon fibers prepared in Example 6 of the present invention.
  • the present invention provides a method for preparing carbon fiber reinforced SiC ceramic matrix composite by 3D printing, and the method includes the following steps:
  • the particle size distribution of the SiC powder can be finely designed through the particle packing density model (such as the multi-element powder particle packing density model modified based on the stovall linear packing theory), so as to optimize the packing behavior of the mixed powder.
  • the specific situation of the particle size distribution in SiC powder is determined as follows: the powder with a particle size of 0.1-2 ⁇ m accounts for 0-5wt% of the total SiC powder, and the powder with a particle size of 2-40 ⁇ m accounts for 22 ⁇ 5% of the total SiC powder.
  • the powder with a particle size of 40 ⁇ 250 ⁇ m accounts for 42 ⁇ 75wt% of the total SiC powder; in order to ensure that the mixed powder has better fluidity and larger bulk density, the particle size distribution in the SiC powder can be further Preferably: the powder with a particle size of 0.1-2 ⁇ m accounts for 0.6-1.8wt% of the total SiC powder, the powder with a particle size of 2-40 ⁇ m accounts for 35-44wt% of the total SiC powder, and the powder with a particle size of 40-250 ⁇ m It accounts for 55-64wt% of the total SiC powder, and the maximum particle size does not exceed 150 ⁇ m.
  • the diameter of the chopped carbon fiber is 0.1-20 ⁇ m, the length-to-diameter ratio is 5 to 500, the addition amount of the chopped carbon fiber accounts for 1-20 wt% of the total SiC powder, and the binder is a ring One or more of oxy resin, phenolic resin or nylon 12, the addition amount of which is 3-20wt% of SiC powder, and the use of horizontal mixing equipment, vertical mixing equipment or three-dimensional mixing equipment for mechanical mixing; Improve the geometric accuracy and mechanical properties of the SiC/chopped carbon fiber green body as much as possible, preferably the chopped carbon fiber with a diameter of 5-10 ⁇ m and an aspect ratio of 100-200, and its addition amount is preferably 4-8wt of the total SiC powder %;
  • the binder is preferably epoxy resin or nylon 12, and the added amount is preferably 6-10 wt% of the mass of the SiC powder.
  • the specific method for laser selective sintering is as follows: first use manual or mechanical method to spread powder, and then slice data based on the three-dimensional model of the target molded body, and irradiate layer by layer with laser according to the slice data A SiC/chopped carbon fiber green body is obtained in a specific area of the powder bed.
  • the type of laser used is preferably a continuous-wavelength CO 2 laser.
  • the organic infiltrant is one or more of epoxy resin solution, phenolic resin solution or asphalt solution, preferably phenolic resin solution or asphalt solution.
  • step (c) the specific process of carbonization treatment or secondary carbonization treatment is: placing the sample to be carbonized in a non-oxidizing atmosphere, heat-treating in a high-temperature furnace, and setting the heating system to be in the binder or Slowly increase the temperature within the pyrolysis temperature range of the carbon precursor, and then quickly increase the temperature to the target temperature of 850°C ⁇ 1100°C and keep it for 1.0h ⁇ 6h for carbonization;
  • the heating rate below 650°C does not exceed 1.5°C/min
  • the target temperature is preferably 950-1000°C
  • the holding time is preferably 2h-3h.
  • step (d) the specific process of the liquid-phase siliconizing method is: burying the SiC/chopped carbon fiber/carbon blank in the metal Si, placing them together in the high-temperature sintering furnace, and starting the vacuuming device to remove the furnace Air, heat the sample and metal Si to the target temperature of 1420°C ⁇ 1800°C and keep it for 0.25h ⁇ 3h; in order to facilitate the full penetration of liquid silicon and avoid excessive sintering of the sample, the target temperature is preferably 1550 ⁇ 1650°C.
  • the time is preferably 0.5h to 1.0h.
  • phase composition distribution of the carbon fiber reinforced SiC ceramic matrix composite material obtained by the above preparation method is shown in Fig. 2, if the relative density is greater than 98%, the flexural strength is greater than 180MPa, and the fracture toughness is greater than 2.5MPa ⁇ m 0.5 .
  • SiC powder with a preset particle size distribution range according to the blending ratio calculated by the model, in which SiC powder with a particle size of 0.1-2 ⁇ m accounts for 0wt%, and SiC powder with a particle size of 2-40 ⁇ m accounts for 55wt%.
  • SiC powder with a particle size of 40 ⁇ 250 ⁇ m accounts for 45% by weight, and then chopped carbon fiber with a diameter of 0.1 ⁇ 20 ⁇ m and an aspect ratio of 5 ⁇ 500, nylon 12 and SiC powder with a preset particle size distribution range are made to 1:20 : 100 mass ratio blended and placed in a drum mixer, add the grinding balls according to the ratio of ball to material ratio of 1:1, and then mechanically mix for 2 hours to obtain SiC-chopped carbon fiber-nylon 12 mixed powder;
  • the laser used in this process is a CO 2 laser with a wavelength range of 9.8 to 10.2 ⁇ m, and the laser spot diameter is 0.15 mm. Its power is 6W, the powder spreading thickness is 0.15mm, the preheating temperature is 145°C, and the scanning rate is 1300mm/s.
  • the laser power at the contour position of the model is 0.5 times that inside the model, and the scanning rate at the contour position of the model is 2 times the inside of the model to obtain the SiC/chopped carbon fiber green body of the target shape;
  • the SiC-chopped carbon fiber-nylon 12 mixed powder has good fluidity, and the prepared SiC/chopped carbon fiber green body has high geometric accuracy, and the dimensional shrinkage rate during the carbonization process is small.
  • Carbon fiber reinforced SiC ceramic matrix composites have high flexural strength and fracture toughness.
  • SiC powder with a particle size of 40 ⁇ 250 ⁇ m accounts for 42wt%, and then chopped carbon fiber with a diameter of 0.1 ⁇ 20 ⁇ m and an aspect ratio of 5 ⁇ 500, phenolic resin (PF) and SiC powder with a preset particle size distribution range are combined with The mass ratio of 20:3:100 is blended and placed in a drum mixer, the grinding balls are added at the ratio of ball to material ratio of 2:1, and then mechanically mixed for 2 hours to obtain SiC-chopped carbon fiber-PF mixed powder;
  • the carbonized body After holding for 1.0h, the carbonized body is obtained; the carbonized body is immersed in the asphalt solution and then placed in the 80°C
  • the vacuum drying box is evacuated to an absolute pressure of less than 0.005MPa, and continuously evacuated under this pressure for 30 minutes to fully infiltrate the asphalt solution into the sample; the green embryo impregnated with the asphalt solution and dried and solidified is placed in a tube furnace, Under Ar atmosphere conditions, the temperature is raised to 850°C at no more than 1.0°C/min, then kept for 0.5h, and then heated to 1100°C for 2.0h for secondary carbonization;
  • SiC powder with a particle size of 40-250 ⁇ m accounts for 75wt%, and then chopped carbon fiber with a diameter of 0.1-20 ⁇ m and a length-to-diameter ratio of 5 to 500, nylon 12 and SiC powder with a preset particle size distribution range are made to 10:12 : 100% mass ratio blended and placed in a drum mixer, add the grinding balls according to the ratio of ball to material ratio of 1:1, and then mechanically mix for 1.0h to obtain SiC- chopped carbon fiber-nylon 12 mixed powder;
  • the laser used in this process is a CO 2 laser with a wavelength range of 9.8 to 10.2 ⁇ m.
  • the laser has a spot diameter of 0.15 mm and its power is 6W.
  • Powder spreading The thickness is 0.15mm, the preheating temperature is 45°C, and the scanning rate is 1300mm/s.
  • the laser power at the contour position of the model is 0.5 times that of the inside of the model, and the scanning rate at the contour position of the model is 2 times that of the inside of the model, resulting in SiC/ Chopped carbon fiber green body;
  • the carbon fiber-reinforced SiC ceramic matrix composite material obtained according to this embodiment has been tested and has a bulk density of 2.70 g ⁇ cm ⁇ 3 , a apparent porosity of 0.27%, a bending strength of 202 MPa, and a fracture toughness of about 3.0 MPa ⁇ m 0.5 .
  • the carbon fiber-reinforced SiC ceramic matrix composite material obtained according to this embodiment has been tested and has a bulk density of 2.64 g ⁇ cm ⁇ 3 , a apparent porosity of 0.36%, a bending strength of 208 MPa, and a fracture toughness of about 3.2 MPa ⁇ m 0.5 .
  • SiC powder with a particle size of 30-150 ⁇ m accounts for 64wt%, and then chopped carbon fiber with a diameter of 5-10 ⁇ m and a length-to-diameter ratio of 100-200, phenolic resin and SiC powder with a preset particle size distribution range to 6:8 : 100 mass ratio blended and placed in a drum mixer, add the grinding balls according to the ratio of ball to material ratio of 4:1, and then mechanically mix for 4 hours to obtain SiC- chopped carbon fiber-phenolic resin mixed powder;
  • the carbon fiber-reinforced SiC ceramic matrix composite material obtained according to this embodiment has been tested and has a bulk density of 2.64 g ⁇ cm ⁇ 3 , a apparent porosity of 0.56%, a bending strength of 190 MPa, and a fracture toughness of about 2.8 MPa ⁇ m 0.5 .
  • Figure 3 is a photo of the microstructure of the SiC/chopped carbon fiber green body obtained in Example 6. It can be seen from the figure that the carbon fiber distribution shape in the SLS preform is complete and the distribution is relatively uniform, showing the powder provided by the present invention The particle size distribution and its mixing method can realize the uniform dispersion of carbon fiber in the material.
  • Figure 4 is a photo of the microstructure of the corrosion section of the carbon fiber reinforced SiC ceramic matrix composite material obtained in Example 6. It can be seen that after the molten silicon is infiltrated into the preform, the internal carbon fiber and the silicified carbon fiber formed by the reaction of the molten silicon still remain relatively high. High aspect ratio, and because its composition is close to the SiC in the material matrix, it has a good interface bond with each other, so it can play a role in crack deflection, bridging and fiber pulling out of the crack in the material, which is conducive to composite Improve the mechanical properties of materials.
  • the obtained mixed powder has better fluidity and larger bulk density than those in Examples 1 to 3.
  • the addition of chopped carbon fiber and binder is optimized to obtain a SiC/chopped carbon fiber green body with higher geometric accuracy and mechanical properties.
  • Examples 4 to 6 have carbonization treatment, The heating temperature and holding time during the secondary carbonization treatment and the liquid phase siliconizing treatment have been further optimized to ensure that the sample does not appear to be cracked, deformed and excessively sintered, and to achieve sufficient carbonization and infiltration.
  • the obtained carbon fiber reinforced SiC ceramic matrix composite The material has higher flexural strength and fracture toughness.

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Abstract

一种3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，该方法包括：将SiC粉体与短切碳纤维、粘结剂混合得到混合粉体；利用混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯；将SiC/短切碳纤维生坯表面清粉后进行碳化处理，然后对其浸渗有机碳前驱体溶液，干燥后进行二次碳化处理得到SiC/短切碳纤维/碳素坯；采用液相渗硅法对其进行致密化处理，获得碳纤维增强SiC陶瓷基复合材料。二次碳化不仅可以借助碳前驱体固化热解后残留相，增大坯体强度便于后续操作，而且有利于短切碳纤维增韧作用的发挥；此外，碳化裂解后形成的空间网状次生碳可以进一步增强复合材料的力学性能。

Description

3D打印制备碳纤维增强SiC陶瓷基复合材料的方法 【技术领域】
本发明属于复合材料领域，更具体地，涉及3D打印制备碳纤维增强SiC陶瓷基复合材料的方法。
【背景技术】
随着航空航天、汽车、空间光学等领域科技水平的快速发展，其核心部件，如高超声速飞行器热防护系统、航空发动机热端部件、高性能刹车系统和空间反射镜等对材料性能的要求愈发苛刻。SiC陶瓷基复合材料以其低密度、高热导、耐烧蚀冲刷和耐磨损等优异性能，有望在上述领域得到成功应用。然而，SiC陶瓷脆性大、裂纹敏感度高，其固有的难加工的特性制约了这种材料被成形为复杂结构零件，极大的限制了其应用范围。对于具有复杂结构的SiC陶瓷材料，传统的加工手段存在工艺复杂、造价高昂的问题。如采用模压或冷等静压得到素坯，再借助数控机床设备(CNC)将其加工成所需形状的成型工艺严重依赖CNC的加工能力，对于一些具有复杂拓扑优化结构(如带有夹层的蜂窝结构)的构件加工成本高昂，有时甚至难以达到设计要求。而采用包括注浆成型、凝胶注模成型以及近年较多采用的直接凝固成型等陶瓷湿法成型技术虽然可以用于制备复杂结构，但这些方法均需借助模具，对于小批量生产来说成本高，不适用于个性化定制。且陶瓷湿法成型技术均需先配制高固相含量、流动性良好的料浆，而实际料浆固相含量很难超过70wt％，因此坯体在后期的固化、脱脂及烧结阶段难以避免一定程度的收缩，样品的几何精度相对较低。
增材制造被列为提升国家竞争力、应对未来挑战亟需发展的先进制造技术，其中激光选区烧结(Selective Laser Sintering，SLS)技术的出现给快速高效成形大型复杂陶瓷零部件带来了新的可能。作为3D打印(增材制造) 技术中的一种，SLS技术适合于快速制造具有复杂结构和特异形状的零部件，能满足整体、分体等各种陶瓷部件的快速成形制造要求；且SLS技术成形过程中不需要设置支撑结构，简化了成形部件的后处理工序，从而有望解决复杂结构SiC陶瓷基复合材料零部件制备所面临的难题。近年来，采用激光选区烧结技术对陶瓷材料进行快速成形研究已有相关报道，如CN200510020015.5公开了一种激光烧结快速成形SiC陶瓷的制备方法，其采用激光烧结技术成形SiC预制体，然后熔渗金属硅并用碱液处理得到复杂形状SiC陶瓷，但是该方法所用的SiC粉末需要经由喷雾造粒来确保较好的流动性，使得该方法所需原料成本高，制备工艺繁琐。
对于SiC陶瓷基复合材料，一个主要的缺点是材料的韧性较差，这限制了由这类材料制备的零件的可靠性。碳纤维是一种重要的一维增强材料，用于传统陶瓷基复合材料力学性能的改善取得了巨大成功。但由于纤维对粉体铺粉性能的不利影响，目前其在基于粉床的激光选区烧结成型上应用较少。文献《Fabrication and characterization of carbon fiber reinforced SiC ceramic matrix composites based on 3D printing technology》(《Journal of the Eueopean Ceramic Society》38，4604-4613)公开了一种基于激光选区烧结结合液相渗硅法制备短切碳纤维增强的SiC复合材料的方法，该方法所用的PF/短切碳纤维-Si(酚醛树脂包覆碳纤维-Si复合粉体)采用溶剂蒸发法制备，同样面临原料成本高，制备工艺繁琐的问题，而且由于其采用短切碳纤维和少量Si粉成形生坯，粉体松装密度低、流动性差，将难以避免成形坯体几何精度差、碳化过程中尺寸收缩率大的问题。
【发明内容】
针对现有技术的上述缺点和/或改进需求，本发明提供了3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其中该方法通过对碳化处理后的生坯浸渗有机碳前驱体溶液并进行二次碳化处理，能够借助碳前驱体固化热解后的残留相，增大坯体强度便于后续操作，并且有效提高短切碳纤维 增强增韧的效果，此外还能利用碳化裂解后形成的空间网状次生碳细化坯体内的孔隙，以此制备具有优异抗折强度和断裂韧性的碳纤维增强SiC陶瓷基复合材料，因而尤其适用于高超声速飞行器热防护系统、航空发动机热端部件、高性能刹车系统、太空望远镜镜坯等零部件的制造。
为实现上述目的，按照本发明的一个方面，本发明提出了一种3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，该方法包括如下步骤：
(a)将SiC粉体与短切碳纤维、粘结剂混合得到混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯；
(c)将所述SiC/短切碳纤维生坯表面清粉后进行碳化处理，然后对其浸渗有机碳前驱体溶液，干燥后进行二次碳化处理得到SiC/短切碳纤维/碳素坯；
(d)采用液相渗硅法对上述SiC/短切碳纤维/碳素坯进行致密化处理，最终获得所述碳纤维增强SiC陶瓷基复合材料。
作为进一步优选地，在步骤(a)中，所述SiC粉体中粒径分布的具体情况为：粒径0.1～2μm的粉体占全部SiC粉体的0～5wt％，粒径2～40μm的粉体占全部SiC粉体的22～55wt％，粒径40～250μm的粉体占全部SiC粉体的42～75wt％。
作为进一步优选地，在步骤(a)中，所述短切碳纤维的直径为0.1～20μm，其长径比为5～500，所述短切碳纤维的加入量占全部SiC粉体的1～20wt％。
作为进一步优选地，在步骤(a)中，所述粘结剂为环氧树脂、酚醛树脂或尼龙12中的一种或多种，其加入量为SiC粉体的3～20wt％。
作为进一步优选地，在所述步骤(b)中，进行激光选区烧结成形的具体方法为：采用人工或者机械方法铺粉，然后基于目标成型体的三维模型得到的切片数据，使用激光逐层照射粉床特定区域得到所述SiC/短切碳纤维生坯。
作为进一步优选地，在步骤(c)中，所述有机碳前驱体溶液为环氧树脂溶液、酚醛树脂溶液或沥青溶液中的一种或多种。
作为进一步优选地，在步骤(c)中，所述碳化处理或二次碳化处理的具体工艺为：将待碳化试样置于非氧化气氛中，在所述粘结剂或者碳前驱体的热解温度范围内缓慢升温，然后快速升温至850℃～1100℃的目标温度并保温1.0h～6h以此进行碳化。
作为进一步优选地，在步骤(d)中，所述液相渗硅法的具体工艺为：将SiC/短切碳纤维/碳素坯埋于金属Si中，然后在真空条件下加热至1420℃～1800℃的目标温度并保温0.25h～3h。
按照本发明的另一方面，提出了一种利用上述方法制备的碳纤维增强SiC陶瓷基复合材料。
总体而言，通过本发明所构思的以上技术方案与现有技术相比，主要具备以下的技术优点：
1.本发明利用有机碳前驱体溶液对碳化处理后的生坯进行浸渗，然后将其加热以此进行二次碳化处理，不仅可以借助碳前驱体固化热解后残留相，增大坯体强度便于后续操作，而且可以利用其裂解生成的次生碳附着于孔隙内基体材料表面，作为“碳消耗层”减轻熔融Si对基体短切碳纤维的破坏，有利于短切碳纤维增韧作用的发挥；此外，碳前驱体碳化裂解后形成的空间网状次生碳可以将坯体内的微米级孔隙进一步细化分割成许多纳米级的孔隙，实现将复合材料内大尺寸残余Si分隔成亚微米或者纳米级Si颗粒的作用，可以进一步增强复合材料的力学性能；
2.尤其是，本发明通过对SiC粉体的粒径分布进行优化，能够有效优化混合粉体的堆积行为，弥补短切碳纤维的加入对混合粉体流动性的不利影响，从而确保混合粉体具有较好的流动性和较大的松装密度，因此只需采用简单的机械混合即能确保混合粉体具有良好流动性能和SLS成形性能，省略了目前陶瓷SLS快速成形过程中原料粉体制备所需的溶解沉淀法或溶 剂蒸发法等繁琐工艺，从而极大地降低了制备成本；
3.此外，本发明通过对3D打印制备碳纤维增强SiC陶瓷基复合材料的工艺过程及工艺参数进行优化，在各工艺参数的共同作用下能够获得相对密度大于98％，抗折强度大于180MPa，断裂韧性大于2.5MPa·m 0.5的碳纤维增强SiC陶瓷基复合材料。
【附图说明】
图1是本发明提供的3D打印制备碳纤维增强SiC陶瓷基复合材料的工艺流程图；
图2是本发明优选实施例制备的碳纤维增强SiC陶瓷基复合材料的物相组成分布示意图；
图3是本发明实施例6中制得含有6wt％短切碳纤维的SiC/短切碳纤维生坯的显微结构照片；
图4是本发明实施例6中制备的含有6wt％短切碳纤维的碳纤维增强SiC陶瓷基复合材料腐蚀断面的显微结构照片。
【具体实施方式】
为了使本发明的目的、技术方案及优点更加清楚明白，以下结合附图及实施例，对本发明进行进一步详细说明。应当理解，此处所描述的具体实施例仅仅用以解释本发明，并不用于限定本发明。此外，下面所描述的本发明各个实施方式中所涉及到的技术特征只要彼此之间未构成冲突就可以相互组合。
如图1所示，本发明提供了一种3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，该方法包括如下步骤：
(a)将SiC粉体与短切碳纤维、粘结剂混合得到混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯；
(c)将SiC/短切碳纤维生坯表面清粉后进行碳化处理，然后对其浸渗 有机碳前驱体溶液，干燥后进行二次碳化处理得到SiC/短切碳纤维/碳素坯；
(d)采用液相渗硅法对上述SiC/短切碳纤维/碳素坯进行致密化处理，最终获得碳纤维增强SiC陶瓷基复合材料。
进一步，在步骤(a)中，可以通过颗粒堆积密度模型(如基于stovall线性堆积理论修正的多元粉体颗粒堆积密度模型)精细设计SiC粉体的粒度分布，从而优化混合粉体的堆积行为，经过计算确定SiC粉体中粒径分布的具体情况为：粒径0.1～2μm的粉体占全部SiC粉体的0～5wt％，粒径2～40μm的粉体占全部SiC粉体的22～55wt％，粒径40～250μm的粉体占全部SiC粉体的42～75wt％；为了确保混合粉体具有较好的流动性和较大的松装密度，SiC粉体中粒径分布可以进一步优选为：粒径0.1～2μm的粉体占全部SiC粉体的0.6～1.8wt％，粒径2～40μm的粉体占全部SiC粉体的35～44wt％，粒径40～250μm的粉体占全部SiC粉体的55～64wt％，且最大粒径不超过150μm。
进一步，在步骤(a)中，短切碳纤维的直径为0.1～20μm，其长径比为5～500，短切碳纤维的加入量占全部SiC粉体的1～20wt％，粘结剂为环氧树脂、酚醛树脂或尼龙12中的一种或多种，其加入量为SiC粉体的3～20wt％，并采用卧式混合设备、立式混合设备或三维式混合设备进行机械混合；为尽可能提高SiC/短切碳纤维生坯的几何精度和力学性能，优选直径5～10μm，长径比100～200范围内的短切碳纤维，其加入量优选为占全部SiC粉体的4～8wt％；粘结剂优选环氧树脂或尼龙12，其加入量优选为SiC粉体质量的6～10wt％。
进一步，在步骤(b)中，进行激光选区烧结成形的具体方法为：首先采用人工或者机械方法铺粉，然后基于目标成型体的三维模型得到的切片数据，并根据切片数据利用激光逐层照射粉床特定区域得到SiC/短切碳纤维生坯，为得到具有较高成型精度的SiC/短切碳纤维生坯，所用激光类型优选连续波长CO 2激光。
进一步，在步骤(c)中，有机浸渗剂为环氧树脂溶液、酚醛树脂溶液或沥青溶液中的一种或多种，优选酚醛树脂溶液或沥青溶液。
进一步，在步骤(c)中，碳化处理或二次碳化处理的具体工艺为：将待碳化试样置于非氧化气氛中，在高温炉中进行热处理，升温制度设定为在粘结剂或者碳前驱体的热解温度范围内缓慢升温，然后快速升温至850℃～1100℃的目标温度并保温1.0h～6h以此进行碳化；
为确保试样不出现开裂变形并且充分碳化，优选650℃以下的升温速率不超过1.5℃/min，目标温度优选为950～1000℃，保温时间优选为2h～3h。
进一步，在步骤(d)中，液相渗硅法的具体工艺为：将SiC/短切碳纤维/碳素坯埋于金属Si中，共同放置于高温烧结炉内，启动抽真空装置排除炉内空气，同时加热试样和金属Si至1420℃～1800℃的目标温度并保温0.25h～3h；为有利于液硅的充分渗透并避免试样过度烧结，目标温度优选为1550～1650℃，保温时间优选为0.5h～1.0h。
利用上述制备方法获得的碳纤维增强SiC陶瓷基复合材料，其物相组成分布如图2所示，如经检测相对密度大于98％，抗折强度大于180MPa，断裂韧性大于2.5MPa·m 0.5。
下面根据具体实施例对本发明作进一步说明。
实施例1
(a)根据模型计算得到的掺混比制备具有预设粒度分布范围的SiC粉体，其中粒径0.1～2μm的SiC粉体占0wt％，粒径2～40μm的SiC粉体占55wt％，粒径40～250μm的SiC粉体占45wt％，然后将直径为0.1～20μm，长径比为5～500的短切碳纤维、尼龙12与具有预设粒度分布范围的SiC粉体以1:20:100的质量比掺混并置于滚筒混合机中，按球料比1:1的比例加入磨球，然后机械混合2h得到SiC-短切碳纤维-尼龙12混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯，该过程中所用的激光为波长范围9.8～10.2μm的CO 2激光，该激光的 光斑直径为0.15mm，其功率为6W，粉末的铺粉厚度为0.15mm，预热温度为145℃，扫描速率为1300mm/s，其中在模型轮廓位置的激光功率为模型内部的0.5倍，模型轮廓位置的扫描速率为模型内部的2倍，得到目标形状的SiC/短切碳纤维生坯；
(c)将上述SiC坯体的表面清粉后置于管式炉中，经2次抽真空-充N 2操作后维持炉内N 2压力不小于1个大气压，然后加热管式炉，以1.05℃/min的升温速率从常温升至200℃，再以1℃/min的升温速率升至480℃，在该温度下保温2h，然后以1.25℃/min的升温速率继续升至650℃，并在该温度下保温0.5h，最后以6.5℃/min的速率升温至850℃，保温6h，得到碳化后的坯体；将碳化后的坯体浸没于热固性酚醛树脂溶液中，然后抽真空至绝对压力小于0.003MPa并在该压力下连续抽真空30min，将浸渗酚醛树脂并干燥固化后的生胚置于管式炉中，在Ar气条件下以不超过1℃/min的升温速率加热管式炉至750℃，然后继续升温至1000℃，保温3h进行二次碳化；
(d)将二次碳化后的坯体埋于一定量金属Si中，共同放置于高温烧结炉内；启动抽真空装置排除炉内空气，同时加热试样和金属Si至1420℃保温3h即得碳纤维增强SiC陶瓷基复合材料。
在制备过程中SiC-短切碳纤维-尼龙12混合粉体具有较好的流动性，制得的SiC/短切碳纤维生坯几何精度高，并且碳化过程中尺寸收缩率较小，同时制得的碳纤维增强SiC陶瓷基复合材料具有较高的抗折强度和断裂韧性。
实施例2
(a)根据模型计算得到的掺混比制备具有预设粒度分布范围的SiC粉体，其中粒径0.1～2μm的SiC粉体占5wt％，粒径2～40μm的SiC粉体占53wt％，粒径40～250μm的SiC粉体占42wt％，然后将直径为0.1～20μm，长径比为5～500的短切碳纤维、酚醛树脂(PF)与具有预设粒度分布范围 的SiC粉体以20:3:100的质量比掺混并置于滚筒混合机中，按球料比2:1的比例加入磨球，然后机械混合2h得到SiC-短切碳纤维-PF混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯，激光选区烧结成形过程中除预热温度为125℃外，其余条件与实施例1相同；
(c)将上述SiC坯体的表面清粉后置于管式炉中，维持炉内Ar气气氛，然后加热管式炉，以不大于1.0℃/min的升温速率将粗坯从常温升至700℃，在该温度下保温1.0h后以6℃/min的速率升温至1100℃，保温1.0h得到碳化后的坯体；碳化后的坯体浸没于沥青溶液中，然后放置于80℃的真空干燥箱内抽真空至绝对压力小于0.005MPa，并在该压力下连续抽真空30min使沥青溶液充分渗入试样内部；将浸渗沥青溶液并干燥固化后的生胚置于管式炉中，在Ar气氛条件下以不超过1.0℃/min升温至850℃后保温0.5h，继续升温至1100℃保温2.0h进行二次碳化；
(d)将二次碳化后的坯体埋于一定量金属Si中，共同放置于高温烧结炉内；启动抽真空装置排除炉内空气，同时加热试样和金属Si至1800℃保温0.25h即得碳纤维增强SiC陶瓷基复合材料。
实施例3
(a)根据模型计算得到的掺混比制备具有预设粒度分布范围的SiC粉体，其中粒径0.1～2μm的SiC粉体占3wt％，粒径2～40μm的SiC粉体占22wt％，粒径40～250μm的SiC粉体占75wt％，然后将直径为0.1～20μm，长径比为5～500的短切碳纤维、尼龙12与具有预设粒度分布范围的SiC粉体以10:12:100的质量比掺混并置于滚筒混合机中，按球料比1:1的比例加入磨球，然后机械混合1.0h得到SiC-短切碳纤维-尼龙12混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯，激光选区烧结成形的实验条件与实施例1相同；
(c)将上述SiC坯体的表面清粉后置于管式炉中，经3次抽真空-充 N 2操作后维持炉内N 2压力不小于1个大气压，然后加热管式炉，以1.05℃/min的升温速率从常温升至200℃，再以1℃/min的升温速率升至480℃，在该温度下保温2h，然后以1.25℃/min的升温速率继续升至650℃，并在该温度下保温0.5h，最后以6.5℃/min的速率升温至1000℃，保温2h，得到碳化后的坯体；将碳化后的坯体浸没于混有8wt％三乙醇胺的环氧树脂溶液中，然后在80℃下快速抽真空至绝对压力小于0.005MPa并保压15min，将浸渗酚醛树脂并干燥固化后的生胚置于管式炉中，在N 2气氛条件下以不超过1℃/min的升温速率加热管式炉至750℃，然后继续升温至850℃，保温6h进行二次碳化；
(d)将二次碳化后的坯体埋于一定量金属Si中，共同放置于高温烧结炉内；启动抽真空装置排除炉内空气，同时加热试样和金属Si至1550℃保温1.0h即得碳纤维增强SiC陶瓷基复合材料。
实施例4
(a)根据模型计算得到的掺混比制备具有预设粒度分布范围的SiC粉体，其中粒径0.1～2μm的SiC粉体占0.6wt％，粒径2～40μm的SiC粉体占44wt％，粒径30～150μm的SiC粉体占55.4wt％，然后将直径为5～10μm，长径比为100～200的短切碳纤维、环氧树脂与具有预设粒度分布范围的SiC粉体以4:6:100的质量比掺混并置于滚筒混合机中，按球料比4:1的比例加入磨球，然后机械混合4h得到SiC-短切碳纤维-环氧树脂混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，该过程中所用的激光为波长范围9.8～10.2μm的CO 2激光，该激光的光斑直径为0.15mm，其功率为6W，粉末的铺粉厚度为0.15mm，预热温度为45℃，扫描速率为1300mm/s，其中在模型轮廓位置的激光功率为模型内部的0.5倍，模型轮廓位置的扫描速率为模型内部的2倍，得到SiC/短切碳纤维生坯；
(c)将上述SiC坯体的表面清粉后置于管式炉中，维持炉内还原性气氛，然后加热管式炉，以1.5℃/min的升温速率将粗坯从常温升至700℃， 在该温度下保温1.0h后以6℃/min的速率升温至950℃，保温3h得到碳化后的坯体；将碳化后的坯体浸没于添加了10wt％稀盐酸的酚醛树脂溶液中，快速抽真空至绝对压力小于1000Pa，并在该压力下连续抽真空30min进行酚醛树脂浸渗，将浸渗酚醛树脂并干燥固化后的试样置于管式炉中进行二次碳化，二次碳化工艺与实施例1中所用二次碳化工艺相同。
(d)将二次碳化后的坯体埋于一定量金属Si中，共同放置于高温烧结炉内；启动抽真空装置排除炉内空气，同时加热试样和金属Si至1650℃保温0.5h即得碳纤维增强SiC陶瓷基复合材料。
根据本实施例得到的碳纤维增强SiC陶瓷基复合材料经检测，其体积密度为2.70g·cm -3，显气孔率为0.27％，抗弯强度达202MPa，断裂韧性约3.0MPa·m 0.5。
实施例5
(a)根据模型计算得到的掺混比制备具有预设粒度分布范围的SiC粉体，其中粒径0.1～2μm的SiC粉体占1.8wt％，粒径2～40μm的SiC粉体占43.2wt％，粒径30～150μm的SiC粉体占55wt％，然后将直径为5～10μm，长径比为100～200的短切碳纤维、环氧树脂与具有预设粒度分布范围的SiC粉体以8:10:100的质量比掺混并置于滚筒混合机中，按球料比4:1的比例加入磨球，然后机械混合4h得到SiC-短切碳纤维-环氧树脂混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，该过程中所采用的工艺条件与参数同实施例4；
(c)将上述SiC坯体的表面清粉后置于管式炉中，维持炉内还原性气氛，然后加热管式炉，以1.5℃/min的升温速率将粗坯从常温升至700℃，在该温度下保温1.0h后以6℃/min的速率升温至1000℃，保温2h得到碳化后的坯体；将碳化后的坯体浸没于添加了12wt％稀盐酸的酚醛树脂溶液中，快速抽真空至绝对压力小于1000Pa，并在该压力下连续抽真空30min进行酚醛树脂浸渗，将浸渗酚醛树脂并干燥固化后的试样置于管式炉中， 在N 2条件下以不超过1.2℃/min升温至850℃后保温1.0h，继续升温至950℃保温3h进行二次碳化；
(d)将二次碳化后的坯体埋于一定量金属Si中，共同放置于高温烧结炉内；启动抽真空装置排除炉内空气，同时加热试样和金属Si至1550℃保温1h即得碳纤维增强SiC陶瓷基复合材料。
根据本实施例得到的碳纤维增强SiC陶瓷基复合材料经检测，其体积密度为2.64g·cm -3，显气孔率为0.36％，抗弯强度达208MPa，断裂韧性约3.2MPa·m 0.5。
实施例6
(a)根据模型计算得到的掺混比制备具有预设粒度分布范围的SiC粉体，其中粒径0.1～2μm的SiC粉体占1wt％，粒径2～40μm的SiC粉体占35wt％，粒径30～150μm的SiC粉体占64wt％，然后将直径为5～10μm，长径比为100～200的短切碳纤维、酚醛树脂与具有预设粒度分布范围的SiC粉体以6:8:100的质量比掺混并置于滚筒混合机中，按球料比4:1的比例加入磨球，然后机械混合4h得到SiC-短切碳纤维-酚醛树脂混合粉体；
(b)利用上述混合粉体进行激光选区烧结成形，该过程除采用的预热温度为125℃外，其余工艺条件与参数同实施例4；
(c)将上述SiC坯体的表面清粉后置于管式炉中，维持炉内还原性气氛，然后加热管式炉，以1.5℃/min的升温速率将粗坯从常温升至700℃，在该温度下保温1.0h后以6℃/min的速率升温至950℃，保温3h得到碳化后的坯体；将碳化后的坯体浸没于沥青中，快速抽真空至绝对压力小于1000Pa，并在该压力下连续抽真空30min使沥青充分渗入试样孔隙内部，将浸渗沥青并干燥固化后的试样置于管式炉中，在埋碳条件下以不超过1.2℃/min升温至850℃后保温1.0h，继续升温至1100℃保温1.0h进行二次碳化；
(d)将二次碳化后的坯体埋于一定量金属Si中，共同放置于高温烧结 炉内进行反应熔渗，该过程所用工艺和参数同实施例4。
根据本实施例得到的碳纤维增强SiC陶瓷基复合材料经检测，其体积密度为2.64g·cm -3，显气孔率为0.56％，抗弯强度达190MPa，断裂韧性约2.8MPa·m 0.5。
图3是实施例6中获得的SiC/短切碳纤维生坯的显微结构照片，从图中可看出SLS成形预制体内碳纤维分布形状完整，分布较为均匀，显示了本发明所给出的粉体粒径分布及其混合方式可以实现碳纤维在材料内部的均匀分散。
图4是实施例6获得的碳纤维增强SiC陶瓷基复合材料腐蚀断面的显微结构照片，可以看到在熔融硅熔渗预制体后，其内部碳纤维与熔融硅反应生成的硅化碳纤维依然保持着较高的长径比，且由于其成分与材料基质中的SiC接近，彼此具有较好的界面结合，因此可以对材料中裂纹扩展起到裂纹偏转、桥接和纤维拔出等阻碍作用，有利于复合材料力学性能的提高。
因实施例4～6中对SiC粉体的粒径分布作了进一步优化，获得的混合粉体相比于实施例1～3具有更好的流动性和较大的松装密度，同时通过对短切碳纤维和粘结剂的添加量进行优化，能够获得具有更高几何精度和力学性能的SiC/短切碳纤维生坯；此外实施例4～6与实施例1～3相比，碳化处理、二次碳化处理以及液相渗硅处理过程中的加热温度和保温时间作了进一步优化，能够保证试样不出现开裂变形和过度烧结，并且实现充分碳化和渗透，获得的碳纤维增强SiC陶瓷基复合材料具有更高的抗折强度和断裂韧性。
本领域的技术人员容易理解，以上所述仅为本发明的较佳实施例而已，并不用以限制本发明，凡在本发明的精神和原则之内所作的任何修改、等同替换和改进等，均应包含在本发明的保护范围之内。

Claims (9)

  1. 一种3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，该方法包括如下步骤：
    (a)将SiC粉体与短切碳纤维、粘结剂混合得到混合粉体；
    (b)利用上述混合粉体进行激光选区烧结成形，得到SiC/短切碳纤维生坯；
    (c)将所述SiC/短切碳纤维生坯表面清粉后进行碳化处理，然后对其浸渗有机碳前驱体溶液，干燥后进行二次碳化处理得到SiC/短切碳纤维/碳素坯；
    (d)采用液相渗硅法对上述SiC/短切碳纤维/碳素坯进行致密化处理，最终获得所述碳纤维增强SiC陶瓷基复合材料。
  2. 如权利要求1所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在步骤(a)中，所述SiC粉体中粒径分布的具体情况为：粒径0.1～2μm的粉体占全部SiC粉体的0～5wt％，粒径2～40μm的粉体占全部SiC粉体的22～55wt％，粒径40～250μm的粉体占全部SiC粉体的42～75wt％。
  3. 如权利要求1所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在步骤(a)中，所述短切碳纤维的直径为0.1～20μm，其长径比为5～500，所述短切碳纤维的加入量占全部SiC粉体的1～20wt％。
  4. 如权利要求1所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在步骤(a)中，所述粘结剂为环氧树脂、酚醛树脂或尼龙12中的一种或多种，其加入量为SiC粉体的3～20wt％。
  5. 如权利要求1所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在所述步骤(b)中，进行激光选区烧结成形的具体方法为：采用人工或者机械方法铺粉，然后基于目标成型体的三维模型得到 的切片数据，使用激光逐层照射粉床特定区域得到所述SiC/短切碳纤维生坯。
  6. 如权利要求1所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在步骤(c)中，所述有机碳前驱体溶液为环氧树脂溶液、酚醛树脂溶液或沥青溶液中的一种或多种。
  7. 如权利要求1所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在步骤(c)中，所述碳化处理或二次碳化处理的具体工艺为：将待碳化试样置于非氧化气氛中，在所述粘结剂或者碳前驱体的热解温度范围内缓慢升温，然后快速升温至850℃～1100℃的目标温度并保温1.0h～6h以此进行碳化。
  8. 如权利要求1～7任一项所述的3D打印制备碳纤维增强SiC陶瓷基复合材料的方法，其特征在于，在步骤(d)中，所述液相渗硅法的具体工艺为：将SiC/短切碳纤维/碳素坯埋于金属Si中，然后在真空条件下加热至1420℃～1800℃的目标温度并保温0.25h～3h。
  9. 一种利用如权利要求1～8任一项所述方法制备的碳纤维增强SiC陶瓷基复合材料。
PCT/CN2020/106966 2019-12-18 2020-08-05 3D打印制备碳纤维增强SiC陶瓷基复合材料的方法 WO2021120636A1 (zh)

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