CN114477999A - 一种耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法 - Google Patents
一种耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法 Download PDFInfo
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- 229910009818 Ti3AlC2 Inorganic materials 0.000 title claims abstract description 37
- 239000000919 ceramic Substances 0.000 title claims abstract description 37
- 230000035939 shock Effects 0.000 title claims abstract description 35
- 238000002360 preparation method Methods 0.000 title claims description 12
- 239000000843 powder Substances 0.000 claims abstract description 62
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 29
- 238000001816 cooling Methods 0.000 claims abstract description 29
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 27
- 238000005245 sintering Methods 0.000 claims abstract description 23
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims abstract description 22
- 239000002041 carbon nanotube Substances 0.000 claims abstract description 20
- 229910021393 carbon nanotube Inorganic materials 0.000 claims abstract description 20
- 239000002202 Polyethylene glycol Substances 0.000 claims abstract description 18
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 238000002156 mixing Methods 0.000 claims abstract description 18
- 229920001223 polyethylene glycol Polymers 0.000 claims abstract description 18
- 239000002994 raw material Substances 0.000 claims abstract description 15
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910001691 hercynite Inorganic materials 0.000 claims abstract description 14
- 229920003257 polycarbosilane Polymers 0.000 claims abstract description 14
- 238000005496 tempering Methods 0.000 claims abstract description 12
- 229910052786 argon Inorganic materials 0.000 claims abstract description 11
- 238000004519 manufacturing process Methods 0.000 claims abstract description 11
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 9
- 239000010439 graphite Substances 0.000 claims abstract description 9
- 238000003754 machining Methods 0.000 claims abstract description 9
- 239000012300 argon atmosphere Substances 0.000 claims abstract description 8
- 238000001035 drying Methods 0.000 claims abstract description 8
- 239000011812 mixed powder Substances 0.000 claims abstract description 8
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 239000002002 slurry Substances 0.000 claims abstract description 8
- 239000003607 modifier Substances 0.000 claims abstract description 5
- 238000011068 loading method Methods 0.000 claims abstract 2
- 229910003079 TiO5 Inorganic materials 0.000 claims description 12
- 239000002245 particle Substances 0.000 claims description 10
- 239000000654 additive Substances 0.000 claims description 7
- 238000000034 method Methods 0.000 claims description 7
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- 239000011863 silicon-based powder Substances 0.000 claims description 3
- 239000002131 composite material Substances 0.000 abstract description 13
- 229910000505 Al2TiO5 Inorganic materials 0.000 abstract description 10
- 238000005303 weighing Methods 0.000 abstract description 8
- 230000007547 defect Effects 0.000 abstract description 6
- 229910010293 ceramic material Inorganic materials 0.000 abstract description 4
- 229910000831 Steel Inorganic materials 0.000 description 15
- 239000010959 steel Substances 0.000 description 15
- 239000000463 material Substances 0.000 description 14
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 10
- 238000012360 testing method Methods 0.000 description 8
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 5
- 229910052749 magnesium Inorganic materials 0.000 description 5
- 239000011777 magnesium Substances 0.000 description 5
- 230000003750 conditioning effect Effects 0.000 description 4
- 238000011049 filling Methods 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000010998 test method Methods 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
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- MHKWSJBPFXBFMX-UHFFFAOYSA-N iron magnesium Chemical compound [Mg].[Fe] MHKWSJBPFXBFMX-UHFFFAOYSA-N 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 231100000241 scar Toxicity 0.000 description 2
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- 208000032544 Cicatrix Diseases 0.000 description 1
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- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 238000002679 ablation Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
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- 150000002500 ions Chemical class 0.000 description 1
- 229910052961 molybdenite Inorganic materials 0.000 description 1
- 229910052982 molybdenum disulfide Inorganic materials 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- AABBHSMFGKYLKE-SNAWJCMRSA-N propan-2-yl (e)-but-2-enoate Chemical compound C\C=C\C(=O)OC(C)C AABBHSMFGKYLKE-SNAWJCMRSA-N 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 230000037387 scars Effects 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
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Abstract
本发明公开了一种耐热震Al2TiO5‑Ti3AlC2陶瓷的制备方法，以Al2TiO5粉体和Ti3AlC2粉体的质量比为（8~9.5）:（2~0.5）作为为原料，2~10wt%的调质剂；调质剂为质量比为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物；在Al2TiO5粉体中加入一半调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余调质剂；然后将粉体总质量0.1~0.5wt%的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.1~0.5wt%的聚乙二醇，与粉体充分混合均匀；混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，用放电等离子进行烧结；通入冷却的氩气快速降温至室温，在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；经车床机加工后为需要的形状。本发明复合材料陶瓷在热震条件下低损伤、少缺陷、可以长期使用，具有较好的应用前景。
Description
技术领域
本发明属于复合陶瓷技术领域。具体涉及一种耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法。
背景技术
目前，冶金行业用高温结构件主要采用耐热钢生产制造，步进式加热炉是钢铁生产工艺主流程中关键设备，其加热钢坯的生产能力、质量和效率直接影响并决定轧钢及生产钢材的产量、质量和效益。步进式加热炉中水冷梁上的耐热钢垫块承托被加热的钢坯，是保障被加热钢坯温度的均匀性及加热质量、保障轧钢生产稳定进行的关键部件。由于耐热钢垫块存在热容高、导热系数大、高温蠕变和氧化损坏等先天性缺陷，易造成被加热钢坯出现“走偏”、与垫块接触部位产生“水冷瘢”（黑印）而影响轧材质量及成材率等突出问题，已成为制约热轧薄板等高技术钢材轧钢生产的“瓶颈”问题。为解决被加热钢坯与垫块接触部位产生的“水冷瘢”（黑印）问题，在不改变加热炉的前提下，常采用提高加热温度和延长加热时间的办法，以保证钢坯达到适当的热塑性和延展性。但此法明显存在能耗高、钢坯烧蚀量大，生产速度慢及效率低，而且耐热钢垫块会因为高温蠕变而被“压扁”损坏，造成被加热钢坯出现“走偏”、堆钢等问题，进而影响加热炉的正常生产，严重制约了行业的技术进步和经济效益。
将具有良好物理化学性能、强度高、高温蠕变性能优异等突出特点的高温陶瓷制造高温陶瓷部件，取代现有的耐热合金钢部件，有望解决耐热合金钢部件带来的突出问题。目前，国内外科研机构已经研究了氧化硅、碳化硅、氮化硅、氧化铝等材料及其复合材料的陶瓷垫块，部分已经获得实际应用，能够改善耐热钢垫块热导率高、高温蠕变性能差等问题。然而实际应用过程中缺陷也很突出：这些高性能结构陶瓷是典型的硬、脆的结构材料，同时温度变化对其弹塑性及高温蠕变性能的影响明显，其材料组成、微结构设计及性能调控一直是其科学研究的难点和热点；相关材料特别是复杂结构、大或小等极限尺寸的高性能陶瓷部件的制备、低损伤、少缺陷、高成品率、高精度加工是亟待突破的共性关键技术。
选择热膨胀系数小的组分一直是改善陶瓷材料的抗热震性、延长其使用寿命的方向之一。Al2TiO5陶瓷具有接近于零的热膨胀系数、低导热系数、高熔点、抗热震和抗热冲击性能优异等特性，是目前低膨胀材料中耐高温性能最好的一种。但由于强度和高温稳定性的原因使钛酸铝陶瓷未能得到广泛应用。Ti3AlC2材料结合了金属与陶瓷的特性，具有较的强度和模量，优异的抗水热氧化性、抗酸碱腐蚀性和抗离子辐照性；同时，像金属一样，可以进行切削加工；另外，Ti3AlC2不仅具备陶瓷所拥有的高屈服强度，高熔点和高热稳定性，还有良好的抗氧化性能；此外，还具备抗腐蚀性能和比MoS2和石墨还优良的自润滑性能。
但是两种材料和复配需要克服较多的技术难题，提高材料的结合性能，需要筛选出较为合适的调质剂和添加剂，以实现两者协同发挥功能的作用。
发明内容
本发明旨在克服现有技术缺陷：提供一种具有高致密度、低热导率、优良高温强度、优异热振稳定性和耐磨性、服役寿命长等特点的Al2TiO5-Ti3AlC2复合材料陶瓷的制备方法。
为实现上述目的，本发明采用的技术方案是：
一种耐热震Al2TiO5-Ti3AlC2复合材料陶瓷的制备方法，包括以下步骤：
（1）原料组成：Al2TiO5粉体和Ti3AlC2粉体的质量比为（8~9.5）:（2~0.5）作为为原料，以2~10wt%的调质剂为外加剂；其中，调质剂为质量比为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物；
（2）原料混合：将步骤（1）中原料和外加剂各自的百分含量比例；首先在Al2TiO5粉体中加入一半调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余调质剂；然后将粉体总质量0.1~0.5wt%的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.1~0.5wt%的聚乙二醇，与粉体充分混合均匀；
（3）成型、烧结与加工：得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，然后用放电等离子进行烧结；
（5）烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；
（6）经车床机加工为需要的形状。
优选的，所述Al2TiO5粉体纯度≥90wt%，粒径小于3mm；所述Ti3AlC2粉体纯度≥90wt%，粒径小于200μm；所述镁铁尖晶石粉体纯度≥92wt%，粒径小于50μm；所述Si粉体纯度≥95wt%，粒径小于10μm；所述模压成型的压力为50~300MPa，保压5-30min；所述氩气纯度≥99%。
所述的放电等离子烧结的过程是：将粉末的模具放入到放电等离子烧结炉中，持续向含模具施加10MPa～150MPa的轴向压力，在真空度为10-4Pa～10Pa下将放电等离子烧结炉内温度以20℃/min～200℃/min的升温速度从室温升温至950℃～1350℃，再在温度为950℃～1350℃下保温2min～30min，再关闭放电等离子烧结炉电源。
本发明与现有技术相比具有以下优点：具体来说，本发明的Al2TiO5-Ti3AlC2复合材料陶瓷具有以下特点：（1）与传统氧化物-碳化物复合材料不同，由于Al2TiO5和Ti3AlC2中共同具备Ti元素和Al元素，Al2TiO5-Ti3AlC2材料的界面在高温高压下能够形成连续化学结合；（2）通过镁铁尖晶石、Al、聚碳硅烷，优选的添加有聚乙二醇、碳纳米管等引入，能够提高复合材料结合性和高温稳定性；（3）Ti3AlC2的金属特性使数控车床机加工性能好和尺寸精确，复合材料陶瓷垫块低损伤、少缺陷、高成品率；（4）本发明Al2TiO5-Ti3AlC2复合材料陶瓷在热震条件下低损伤、少缺陷、可以长期使用，具有较好的应用前景。基于两种材料的特性，本发明Al2TiO5-Ti3AlC2复合材料陶瓷垫块是在热膨胀系数低的Al2TiO5材料中构建高强度、高韧性的Ti3AlC2结合相网络，提升材料的致密度、高温强度、热振稳定性和耐磨性，从而延长陶瓷服役寿命。
具体实施方式
为避免重复，本具体实施方式中：Al2TiO5粉体纯度≥90wt%，粒径小于3mm；Ti3AlC2粉体纯度≥90wt%，粒径小于200μm；调质剂为质量比为1：1：5的镁铁尖晶石、Si和聚乙二醇的混合物；镁铁尖晶石粉体纯度≥92wt%，粒径小于50μm；Si粉体纯度≥95wt%，粒径小于10μm；氩气纯度≥99%。实施例中不再赘述。
为避免重复，没有特别提及的情况下，采用下列方法测试复合材料陶瓷垫块的性能参数：
按照GB/T 25995-2010 精细陶瓷密度和显气孔率试验方法，测试气孔率。
按照GB/ T 4741-1999 陶瓷材料抗弯曲强度试验方法，测试抗折强度。
参照GB/T16535-1996工程陶瓷线热膨胀系数试验方法，测试热膨胀系数。测试温度范围按下述实验设定。
参照GB/T 16536-1996 工程陶瓷抗热震性试验方法，测试热震断裂次数，测试温度范围按照下述实验设定，水冷为15摄氏度。
实施例1
称取80wt%的Al2TiO5粉体和20wt%的Ti3AlC2粉体为原料，首先在Al2TiO5粉体中加入1wt%的调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余1wt%的调质剂，所述调质剂为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物。
将粉体总质量0.1%的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.1wt％的聚乙二醇，与粉体充分混合均匀充分混合。
得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，模压成型的压力为100MPa，保压25min。然后用放电等离子进行烧结。
烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；经车床机加工为需要的形状。
气孔率为4.01％，抗折强度为120.5MPa，热膨胀系数α为1.31×10-6/℃(室温～1000℃)，热震断裂次数为500次(1100℃～室温水冷)。
对比例1
与实施例1不同的是，称取80wt%的Al2TiO5粉体和20wt%的Ti3AlC2粉体为原料。不添加调质剂。将粉体总质量0.1%的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.1wt％的聚乙二醇，与粉体充分混合均匀充分混合。
得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，模压成型的压力为100MPa，保压25min。然后用放电等离子进行烧结。烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；经车床机加工为需要的形状。
经过测试，气孔率为7.02％，抗折强度为98.5MPa，热膨胀系数α为1.27×10-6/℃(室温～1000℃)，热震断裂次数为469次(1100℃～室温水冷)。因为不加入调质剂，其粉体的结合情况较差，气孔率较高，影响了物理性能。
对比例2
与实施例1不同的是，称取80wt%的Al2TiO5粉体和20wt%的Ti3AlC2粉体为原料，首先在Al2TiO5粉体中加入1wt%的调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余1wt%的调质剂，所述调质剂为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物。
不添加碳纳米管和聚乙二醇。得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，模压成型的压力为100MPa，保压25min。然后用放电等离子进行烧结。烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；经车床机加工为需要的形状。
气孔率为3.98％，抗折强度为87.5MPa，热膨胀系数α为1.22×10-6/℃(室温～1000℃)，热震断裂次数为250次(1100℃～室温水冷)。
对比可以得出，不添加碳纳米管和聚乙二醇，虽然不会大幅度影响气孔率和抗折强度等指标，但是会极大的影响热震断裂次数，说明碳纳米管可以作为增强相，提高热震性能。
实施例2
称取95wt%的Al2TiO5粉体和5wt%的Ti3AlC2粉体为原料，首先在Al2TiO5粉体中加入5wt%的调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余5wt%的调质剂，所述调质剂为1：1：5的镁铁尖晶石、铝和聚碳硅烷的混合物。
将粉体总质量0.5%的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.1wt％的聚乙二醇，与粉体充分混合均匀充分混合。
得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，模压成型的压力为100MPa，保压25min。然后用放电等离子进行烧结。
烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；经车床机加工为需要的形状。
气孔率为3.85％，抗折强度为126.5MPa，热膨胀系数α为1.26×10-6/℃(室温～1000℃)，热震断裂次数为550次(1100℃～室温水冷)。
提高调质剂和碳纳米管的添加量，可以改善陶瓷的综合性能，具体表现为气孔率下降，强度上升，最主要的指标热震断裂次数提高。
实施例3
以87wt%的Al2TiO5粉体和13wt%的Ti3AlC2粉体为原料，以6wt%的调质剂为外加剂；其中，调质剂为质量比为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物；
原料和外加剂各自的百分含量比例；首先在Al2TiO5粉体中加入一半调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余调质剂；然后将粉体总质量0.3%的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.3wt％的聚乙二醇，与粉体充分混合均匀；得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，然后用放电等离子进行烧结；烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；经车床机加工为需要的形状。
气孔率为5.05％，抗折强度为92.5MPa，热膨胀系数α为1.22×10-6/℃(室温～1000℃)，热震断裂次数为510次(1100℃～室温水冷)。
在合理的范围内调整调质剂和碳纳米管的添加量，可以获得抗热震性能较佳的产品。
对比例3
与实施例3不同的是，仅仅分别设定调质剂如下，其它不变，
（1）1：1：4的镁铁尖晶石、Al和聚碳硅烷的混合物；
经测试，气孔率为5.86％，抗折强度为89.4MPa，热膨胀系数α为1.29×10-6/℃(室温～1000℃)，热震断裂次数为480次(1100℃～室温水冷)。性能有所下降。
（2）1：1：6的镁铁尖晶石、Al和聚碳硅烷的混合物；
经测试，气孔率为5.94％，抗折强度为87.3MPa，热膨胀系数α为1.32×10-6/℃(室温～1000℃)，热震断裂次数为450次(1100℃～室温水冷)。过量添加聚碳硅烷会影响热震性能。
（3）1：1的镁铁尖晶石和铝
经测试，气孔率为8.54％，抗折强度为60.3MPa，热膨胀系数α为1.27×10-6/℃(室温～1000℃)，热震断裂次数为350次(1100℃～室温水冷)。不添加聚碳硅烷会对热震性能产生较大的影响。
（4）1：5的铝和聚碳硅烷
经测试，气孔率为9.03％，抗折强度为59.6MPa，热膨胀系数α为1.20×10-6/℃(室温～1000℃)，热震断裂次数为410次(1100℃～室温水冷)。不添加镁铁尖晶石，会增大气孔率，对热震性能稍有影响。
综上，本发明所采用的质量比为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物综合性能最佳。
上述实施例是对本发明技术方案的解释，本发明的保护范围以权利要求书的内容为准。
Claims (8)
1.一种耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，其特征在于，包括以下步骤：
（1）原料组成：Al2TiO5粉体和Ti3AlC2粉体的质量比为（8~9.5）:（2~0.5）作为为原料，以2~10wt%的调质剂为外加剂；其中，调质剂为质量比为1：1：5的镁铁尖晶石、Al和聚碳硅烷的混合物；
（2）原料混合：按照步骤（1）中原料和外加剂各自的比例；首先在Al2TiO5粉体中加入一半调质剂混合，混合均匀后再依次加入Ti3AlC2粉体和剩余调质剂；然后将粉体总质量0.1~0.5wt％的碳纳米管分散于乙醇中，得到碳纳米管浆料，再称取粉体重量的0.1~0.5wt％的聚乙二醇，将所述浆料、聚乙二醇与粉体充分混合均匀；
（3）成型、烧结与加工：得到的混合粉料装入石墨模具中，干燥脱水脱醇，冷压成型，然后用放电等离子烧结；
（5）烧结后，通入冷却的氩气快速降温至室温，再在氩气气氛下升温1200~1300℃保温24~48h，缓慢冷却得到的烧结坯体；
（6）经车床机加工后为需要的形状。
2.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，其特征在于，所述Al2TiO5粉体纯度≥90wt%，粒径小于3mm。
3.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，，其特征在于，所述Ti3AlC2粉体纯度≥90wt%，粒径小于200μm。
4.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，，其特征在于，所述镁铁尖晶石粉体纯度≥92wt%，粒径小于50μm。
5.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，其特征在于，所述Si粉体纯度≥95wt%，粒径小于10μm。
6.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，其特征在于，所述模压成型的压力为50~300MPa，保压5-30min。
7.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，其特征在于，所述氩气纯度≥99%。
8.根据权利要求1所述耐热震Al2TiO5-Ti3AlC2陶瓷的制备方法，其特征在于，所述放电等离子烧结的过程是，将装有粉末的模具放入到放电等离子烧结炉中，持续向含模具施加10MPa～150MPa的轴向压力，在真空度为10-4Pa～10Pa下将放电等离子烧结炉内温度以20℃/min～200℃/min的升温速度从室温升温至950℃～1350℃，在温度为950℃～1350℃下保温2min～30min，关闭放电等离子烧结炉电源。
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| 袁蝴蝶等: "Ti3SiC2、Ti3AlC2复相材料高温抗氧化行为的研究", 《热加工工艺》 * |
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Denomination of invention: A preparation method for heat-resistant and shock-absorbing Al2TiO5-Ti3AlC2 ceramics Granted publication date: 20220920 Pledgee: Industrial Bank Co.,Ltd. Taizhou Branch Pledgor: TAIZHOU HONGHUA METALLURGICAL MACHINERY CO.,LTD. Registration number: Y2024980016529 |