CN107244918B - 一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法 - Google Patents
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法 Download PDFInfo
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- 239000000919 ceramic Substances 0.000 title claims abstract description 69
- 239000002131 composite material Substances 0.000 title claims abstract description 52
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- 239000000843 powder Substances 0.000 claims abstract description 70
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- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 36
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical group CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 28
- 238000010438 heat treatment Methods 0.000 claims description 26
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- 229910033181 TiB2 Inorganic materials 0.000 claims description 15
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- 229910010293 ceramic material Inorganic materials 0.000 abstract description 4
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- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 12
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- 239000010439 graphite Substances 0.000 description 12
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- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 12
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- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 5
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
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- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
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Abstract
本发明涉及一种TiB‑TiC‑TiB2‑B4C‑Al复合陶瓷的快速制备方法,属于功能防护材料制备领域。该方法是将TC4粉、Al粉、TiB2粉和B4C粉加入球磨罐中,加入球磨介质,球磨至混合均匀,干燥,得到混合粉体;采用放电等离子烧结系统对所述混合粉体进行烧结处理,得到所述复合陶瓷;该方法制备得到的复合陶瓷致具有更高的强度,高温硬度,断裂韧性和耐磨性,总体性能提升很大,是未来复合防护材料中陶瓷材料的理想选择。
Description
技术领域
本发明涉及一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,属于功能防护材料制备领域。
背景技术
金属陶瓷既保持陶瓷的高强度,高硬度,耐高温,化学稳定性强等优点,又有较好的韧性以及可塑性,是一类非常重要的工具材料和结构材料。其用途极其广泛,几乎涉及到国民经济的各个部门和现代技术的各个领域,对工业的发展和生产率的提高起着重要的推动作用。
其中,碳化钛和硼化钛是近年来发展较快的两类金属陶瓷。熔点高,耐磨性好,硬度大等一系列优点使得碳化钛(TiCp)在切削工具,喷沙嘴等结构材料等方面广泛使用。钛的硼化物(TiBw)具有较高熔点,高硬度,良好的导电性,可用电加工手段成型,但是硼化钛自扩散系数低,使得其可烧结性受到很大影响且断裂韧性比较差,在很大程度上限制了应用。
最近研究表明在陶瓷材料中添加金属(铝),这部分金属颗粒可通过塑性变形、剥离、拔出,可阻止裂纹扩展作用,使陶瓷材料的室温与高温韧性提高,金属与陶瓷基体新生相的钉扎也能阻止裂纹扩展,提高韧性。此外,钉扎效应还可抑制颗粒的异常长大,细化复合材料晶粒,提高高温强度,提高致密度和比强度。
但是,由于TiB-TiC-TiB2-B4C-Al复相陶瓷制备工艺复杂,成本高,产物成品率不高,截止目前为止,还没有将其应用到防护材料的报导。
发明内容
有鉴于此,本发明的目的是提供一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法采用放电等离子烧结系统,通过TC4粉、Al粉、TiB2和 B4C粉在较低的温度下发生的原位反应,实现TiB-TiC-TiB2-B4C-Al复合陶瓷的快速可控低成本制备。最终的烧结产物兼具TiB、TiB2与TiC单相陶瓷的优点,而且与单相陶瓷相比,具有更高的强度,高温硬度,断裂韧性和耐磨性,总体性能提升很大,是未来复合防护材料中陶瓷材料的理想选择。
本发明的目的由以下技术方案实现。
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将TC4粉、Al粉、TiB2粉和B4C粉加入球磨罐中,球磨至混合均匀,得到混合泥浆,干燥,得到混合粉体;
其中,TC4粉、B4C粉和TiB2粉的质量比为1:(1.5~8):(7.5~1);Al 粉的质量为混合粉体质量的0.3%~30%;
优选TC4粉的粒径≤60μm;优选TiB2粉的粒径≤20μm;优选B4C粉的粒径≤15μm;优选Al粉的粒径≤80μm;
优选球磨采用SM-QB行星式球磨机;
优选球磨参数为:球磨介质为无水乙醇;球料比为3:1;球磨机转速为300 r/min,球磨时间为0.5h~1h;
优选磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为 10mm,小玛瑙球的直径为5mm;
优选干燥为:
先将混合泥浆于70℃~80℃下真空干燥至球磨介质挥发完毕,再于 30℃~80℃干燥0.5h~1h;
优选真空干燥采用真空旋转蒸发仪,转速为40r/min~100r/min;
(2)采用放电等离子烧结系统对混合粉体进行烧结处理,得到本发明所述 TiB-TiC-TiB2-B4C-Al复合陶瓷。
其中,烧结过程为:
在初始真空度<15Pa,初始压力为0.2MPa~1MPa下,以60℃/min~ 120℃/min的升温速率升温;当温度升至600℃~630℃时,调节升温速率为 20℃/min以下;当温度高于680℃,且烧结的混合粉体位移率变化量≤0.02 mm/s时,调节升温速率为30℃/min~100℃/min;当温度升至800℃~850℃时,调节升温速率为10℃/min~20℃/min,当温度高于1000℃且真空度<15Pa 时,调节升温速率为30℃/min~60℃/min,并同时加压,待温度升至1050℃~ 1750℃,压力达5MPa~50MPa后,保温保压3min~15min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,随炉冷却至100℃以下。
有益效果
1.本发明提供了一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法选用TC4粉、Al粉、TiB2粉和B4C粉的混合粉末为原料,采用放电等离子烧结系统进行烧结,电场会在烧结过程中清洁和活化所述混合粉末的颗粒表面,使混合粉末在较低的烧结温度下充分反应,烧结得到的TiB-TiC-TiB2-B4C-Al复合陶瓷致密度高,韧性好,强度高,综合性能良好;所述TiB-TiC-TiB2-B4C-Al 复合陶瓷致密度高达99.3%,动态压缩强度值高达1900MPa,可应用于防护材料领域;
2.本发明提供了一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法简单易行,周期短,实用性强,有利于工业化。
附图说明
图1为实施例1~6中制备的TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度与致密度值。
具体实施方式
下面结合附图和具体实施例对本发明作详细的阐述。
以下实施例中所述TC4粉由北京泰欣隆有限公司生产,平均粒径为45μm,纯度≥99.8%;其中各组分及质量分数(wt%)如表1所示:
表1
所述B4C粉由牡丹江金刚钻碳化硼有限公司生产,其平均粒径为10μm,纯度为99.8%;
所述Al粉由河南远洋铝业有限公司生产,平均粒径为20μm,纯度为99.5%;其中各组分及质量分数(wt%)如表2所示:
表2
所述TiB2粉由丹东日进科技有限公司生产,平均粒径为3μm,纯度为 99.8%。
所述无水乙醇由北京市通广精细化工公司生产。
所述复合陶瓷理论密度计算公式:
其中,M总为混合粉总质量,MTiB、MTiB2、MAl、MB4C和MTiC依次分别为 TiB、TiB2、Al、B4C和TiC的理论质量,ρTiB=4.50g/cm3,ρTiB2=4.51g/cm3,ρAl=2.7g/cm3,ρB4C=2.52g/cm3,ρTiC=4.93g/cm3。
所述动态压缩强度的测量采用分离式Hopkinson压杆装置(SHPB)。
所述实际密度根据国标GB/T 1423-1996《贵金属及其合金密度的测试方法》中规定的方法进行。
所述致密度D的计算公式为:D=ρ实际/ρ理论×100%,其中,ρ实际表示实际密度,ρ理论表示理论密度。
实施例1
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将9.97g TC4粉、64.80g B4C粉、24.93g TiB2粉和0.3g Al粉加入 SM-QB行星式球磨机的球磨罐中,并按球料比为3:1加入磨球和过量的无水乙醇;在300r/min的转速下,球磨0.5h混合均匀,得到混合泥浆;将所述混合泥浆倒入真空旋转蒸发仪中,在转速为100r/min、水浴温度为80℃条件下转蒸 0.5h,得到混合粉末前体;将混合粉末前体放入电热恒温鼓风干燥箱中,于60℃下干燥1h,得到混合粉末。
其中,磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
(2)将100g混合粉末放入内径为60mm的石墨模具中,再用石棉毡包裹石墨模具,放入放电等离子烧结系统中,设置炉腔内初始真空度<15Pa,初始压力为0.2MPa,先以60℃/min的升温速率进行升温,当温度升至600℃时,调节升温速率为10℃/min;当温度高于680℃,且烧结的混合粉体位移率变化量≤0.02mm/s时,调节升温速率为30℃/min;当温度升至800℃时,原位反应开始发生,此阶段有明显放气现象,炉腔内气压值升高,调节升温速率为10℃/min,当温度高于1000℃、且真空度<15Pa时,调节升温速率为60℃/min,并同时加压,待温度升至1650℃,压力达20MPa后,保温保压3min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,再随炉冷却至100℃以下,取出烧结后的陶瓷块体,使用乙醇和去离子水清洗陶瓷的表面,得到 TiB-TiC-TiB2-B4C-Al复合陶瓷。
所述TiB-TiC-TiB2-B4C-Al复合陶瓷的实际密度为2.94g/cm3,理论密度为 2.96g/cm3;如图1所示,TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度为12.0mm,致密度为99.3%,动态压缩强度值为1350MPa。
实施例2
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将7g TC4粉、45.5g B4C粉、17.5g TiB2粉和30g Al粉加入SM-QB 行星式球磨机的球磨罐中,并按球料比为3:1加入磨球和过量的无水乙醇;在 300r/min的转速下,球磨0.5h混合均匀,得到混合泥浆;将所述混合泥浆倒入真空旋转蒸发仪中,在转速为100r/min、水浴温度为80℃条件下转蒸0.5h,得到混合粉末前体;将混合粉末前体放入电热恒温鼓风干燥箱中,于60℃下干燥1h,得到混合粉末。
其中,磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
(2)将100g混合粉末放入内径为60mm的石墨模具中,再用石棉毡包裹石墨模具,放入放电等离子烧结系统中,设置炉腔内初始真空度<15Pa,初始压力为1MPa,先以120℃/min的升温速率升温,当温度升至630℃时,调节升温速率为20℃/min;当温度高于680℃,且烧结的混合粉体位移率变化量≤ 0.02mm/s时,调节升温速率为100℃/min;当温度升至800℃时,原位反应开始发生,此阶段有明显放气现象,炉腔内气压值升高,调节升温速率为20℃/min,当温度高于1000℃、且真空度<15Pa时,调节升温速率为60℃/min,并同时加压,待温度升至1550℃,压力达20MPa后,保温保压15min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,再随炉冷却至100℃以下,取出烧结后的陶瓷块体,使用乙醇和去离子水清洗陶瓷的表面,得到 TiB-TiC-TiB2-B4C-Al复合陶瓷。
所述TiB-TiC-TiB2-B4C-Al复合陶瓷的实际密度为2.92g/cm3,理论密度为 2.94g/cm3;如图1所示,TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度为12.1mm,致密度为99.3%,动态压缩强度值为1900MPa。
实施例3
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将9.97g TC4粉、14.96g B4C粉、74.77g TiB2粉和0.3g Al粉加入 SM-QB行星式球磨机的球磨罐中,并按球料比为3:1加入磨球和过量的无水乙醇;在300r/min的转速下,球磨0.5h混合均匀,得到混合泥浆;将所述混合泥浆倒入真空旋转蒸发仪中,在转速为100r/min、水浴温度为80℃条件下转蒸 0.5h,得到混合粉末前体;将混合粉末前体放入电热恒温鼓风干燥箱中,于60℃下干燥1h,得到混合粉末。
其中,磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
(2)将100g混合粉末放入内径为60mm的石墨模具中,再用石棉毡包裹石墨模具,放入放电等离子烧结系统中,设置炉腔内初始真空度<15Pa,初始压力为0.2MPa,先以60℃/min的升温速率升温,当温度升至600℃时,调节升温速率为10℃/min;当温度高于680℃,且烧结的混合粉体位移率变化量≤ 0.02mm/s时,调节升温速率为30℃/min;当温度升至800℃时,原位反应开始发生,此阶段有明显放气现象,炉腔内气压值升高,调节升温速率为10℃/min,当温度高于1000℃、且真空度<15Pa时,调节升温速率为60℃/min,并同时加压,待温度升至1750℃,压力达50MPa后,保温保压3min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,再随炉冷却至100℃以下,取出烧结后的陶瓷块体,使用乙醇和去离子水清洗陶瓷的表面,得到 TiB-TiC-TiB2-B4C-Al复合陶瓷。
所述TiB-TiC-TiB2-B4C-Al复合陶瓷的实际密度为3.96g/cm3,理论密度为 4.03g/cm3;如图1所示,TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度为8.9mm,致密度为98.3%。
实施例4
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将7g TC4粉、10.5g B4C粉、52.5g TiB2粉和30g Al粉加入SM-QB 行星式球磨机的球磨罐中,并按球料比为3:1加入磨球和过量的无水乙醇;在 300r/min的转速下,球磨0.5h混合均匀,得到混合泥浆;将所述混合泥浆倒入真空旋转蒸发仪中,在转速为100r/min、水浴温度为80℃条件下转蒸0.5h,得到混合粉末前体;将混合粉末前体放入电热恒温鼓风干燥箱中,于60℃下干燥1h,得到混合粉末。
其中,磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
(2)将100g混合粉末放入内径为60mm的石墨模具中,再用石棉毡包裹石墨模具,放入放电等离子烧结系统中,设置炉腔内初始真空度<15Pa,初始压力为1MPa,先以120℃/min的升温速率进行升温,当温度升至630℃时,调节升温速率为20℃/min;当温度高于680℃,且烧结的混合粉体位移率变化量≤0.02mm/s时,调节升温速率为100℃/min;当温度升至800℃时,原位反应开始发生,此阶段有明显放气现象,炉腔内气压值升高,调节升温速率为20℃ /min,当温度高于1000℃、且真空度<15Pa时,调节升温速率为60℃/min,并同时加压,待温度升至1750℃,压力达5MPa后,保温保压15min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,再随炉冷却至100℃以下,取出烧结后的陶瓷块体,使用乙醇和去离子水清洗陶瓷的表面,得到 TiB-TiC-TiB2-B4C-Al复合陶瓷。
所述TiB-TiC-TiB2-B4C-Al复合陶瓷的实际密度为3.49g/cm3,理论密度为 3.51g/cm3;如图1所示,TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度为10.1mm,致密度为99.4%。
实施例5
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将9.97g TC4粉、79.76g B4C粉、9.97g TiB2粉和0.3g Al粉加入SM-QB 行星式球磨机的球磨罐中,并按球料比为3:1加入磨球和过量的无水乙醇;在 300r/min的转速下,球磨0.5h混合均匀,得到混合泥浆;将所述混合泥浆倒入真空旋转蒸发仪中,在转速为100r/min、水浴温度为80℃条件下转蒸0.5h,得到混合粉末前体;将混合粉末前体放入电热恒温鼓风干燥箱中,于60℃下干燥1h,得到混合粉末。
其中,磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
(2)将100g混合粉末放入内径为60mm的石墨模具中,再用石棉毡包裹石墨模具,放入放电等离子烧结系统中,设置炉腔内初始真空度<15Pa,初始压力为1MPa,先以120℃/min的升温速率进行升温,当温度升至630℃时,调节升温速率为20℃/min;当温度高于680℃,且烧结的混合粉体位移率变化量≤0.02mm/s时,调节升温速率为100℃/min;当温度升至800℃时,原位反应开始发生,此阶段有明显放气现象,炉腔内气压值升高,调节升温速率为20℃ /min,当温度高于1000℃、且真空度<15Pa时,调节升温速率为60℃/min,并同时加压,待温度升至1750℃,压力达5MPa后,保温保压15min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,再随炉冷却至100℃以下,取出烧结后的陶瓷块体,使用乙醇和去离子水清洗陶瓷的表面,得到 TiB-TiC-TiB2-B4C-Al复合陶瓷。
所述TiB-TiC-TiB2-B4C-Al复合陶瓷的实际密度为2.71g/cm3,理论密度为 2.76g/cm3;如图1所示,TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度为13.1mm,致密度为98.2%。
实施例6
一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,所述方法步骤如下:
(1)将7g TC4粉、56g B4C粉、7g TiB2粉和30g Al粉加入SM-QB行星式球磨机的球磨罐中,并按球料比为3:1加入磨球和过量的无水乙醇;在300 r/min的转速下,球磨0.5h混合均匀,得到混合泥浆;将所述混合泥浆倒入真空旋转蒸发仪中,在转速为100r/min、水浴温度为80℃条件下转蒸0.5h,得到混合粉末前体;将混合粉末前体放入电热恒温鼓风干燥箱中,于60℃下干燥1 h,得到混合粉末。
其中,磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
(2)将100g混合粉末放入内径为60mm的石墨模具中,再用石棉毡包裹石墨模具,放入放电等离子烧结系统中,设置炉腔内初始真空度<15Pa,初始压力为1MPa,先以120℃/min的升温速率进行升温,当温度升至630℃时,调节升温速率为20℃/min;当温度高于680℃,且烧结的混合粉体位移率变化量≤0.02mm/s时,调节升温速率为100℃/min;当温度升至800℃时,原位反应开始发生,此阶段有明显放气现象,炉腔内气压值升高,调节升温速率为20℃ /min,当温度高于1000℃、且真空度<15Pa时,调节升温速率为60℃/min,并同时加压,待温度升至1750℃,压力达5MPa后,保温保压15min;然后保持压力不变,随炉冷却至900℃以下,卸除压力,再随炉冷却至100℃以下,取出烧结后的陶瓷块体,使用乙醇和去离子水清洗陶瓷的表面,得到 TiB-TiC-TiB2-B4C-Al复合陶瓷。
所述TiB-TiC-TiB2-B4C-Al复合陶瓷的实际密度为2.70g/cm3,理论密度为 2.74g/cm3;如图1所示,TiB-TiC-TiB2-B4C-Al复合陶瓷的厚度为13.1mm,致密度为98.5%。
本发明包括但不限于以上实施例,凡是在本发明精神的原则之下进行的任何等同替换或局部改进,都将视在本发明的保护范围之内。
Claims (9)
1.一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:所述方法步骤如下:
(1)将TC4粉、Al粉、TiB2粉和B4C粉加入球磨罐中,球磨使其混合均匀,得到混合泥浆,干燥,得到混合粉体;
TC4粉、B4C粉和TiB2粉的质量比为1:(1.5~8):(7.5~1);Al粉的质量为混合粉体质量的0.3 %~30 %;
(2)采用放电等离子烧结系统对混合粉体进行烧结处理,得到所述TiB-TiC-TiB2-B4C-Al复合陶瓷;
烧结过程为:在初始真空度<15 Pa,初始压力为0.2MPa~1MPa下,以60 ℃/min~120℃/min的升温速率升温;当温度升至600 ℃~630 ℃时,调节升温速率为20 ℃/min以下;当温度高于680 ℃,且烧结的混合粉体位移率变化量≤0.02 mm/s时,调节升温速率为30℃/min~100 ℃/min;当温度升至800 ℃~850 ℃时,调节升温速率为10 ℃/min~20 ℃/min,当温度高于1000 ℃且真空度<15Pa时,调节升温速率为30 ℃/min~60 ℃/min,并同时加压,待温度升至1050 ℃~1750 ℃,压力达5MPa~50MPa后,保温保压3min~15min;然后保持压力不变,随炉冷却至900 ℃以下,卸除压力,随炉冷却至100 ℃以下。
2.根据权利要求1所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:TC4粉的粒径≤60μm;TiB2粉的粒径≤20μm;B4C粉的粒径≤15μm;Al粉的粒径≤80μm。
3.根据权利要求1或2所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:球磨介质为无水乙醇;球料比为3:1;球磨机转速为300r/min,球磨时间为0.5 h~1h。
4.根据权利要求1或2所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:球磨使用的磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
5.根据权利要求1或2所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:将混合泥浆于70 ℃~80 ℃下真空干燥至球磨介质挥发完毕,再于30 ℃~80 ℃干燥0.5 h~1h。
6.根据权利要求5所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:真空干燥采用真空旋转蒸发仪,转速为40r/min~100r/min。
7.根据权利要求1或2所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:球磨介质为无水乙醇;球料比为3:1;球磨机转速为300r/min,球磨时间为0.5 h~1h;球磨使用的磨球由质量比为1:1的大玛瑙球和小玛瑙球组成,大玛瑙球的直径为10mm,小玛瑙球的直径为5mm。
8.根据权利要求7所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:将混合泥浆于70 ℃~80 ℃下真空干燥至球磨介质挥发完毕,再于30 ℃~80 ℃干燥0.5 h~1h。
9.根据权利要求8所述的一种TiB-TiC-TiB2-B4C-Al复合陶瓷的快速制备方法,其特征在于:真空干燥采用真空旋转蒸发仪,转速为40r/min~100r/min。
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