CN114149269B - 铝电解槽侧墙用AlN-SiC固溶体结合SiC复合耐火材料及制备方法 - Google Patents
铝电解槽侧墙用AlN-SiC固溶体结合SiC复合耐火材料及制备方法 Download PDFInfo
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Abstract
本发明属于耐火材料领域,尤其涉及一种铝电解槽侧墙用AlN‑SiC固溶体结合SiC复合耐火材料及其制备方法。所述AlN‑SiC固溶体结合SiC复合耐火材料包括如下原料组成:65~90wt%的碳化硅、5~20wt%的铝粉、5~10wt%的硅粉、0~5wt%的碳粉,外加2~5wt%的结合剂。将上述原料与结合剂混合均匀后压制成型并干燥,得到低碳Al‑Si‑SiC复合坯体,于1450℃~2000℃埋碳气氛下烧成,制得AlN‑SiC固溶体结合SiC复合耐火材料。本发明针对现有技术中铝电解槽用Si3N4‑SiC复合材料中的Si3N4结合相在服役过程中易与Al液、冰晶石等发生反应,导致材料结构破坏、使用性能大大降低,创新地在Si‑SiC复合体系中进一步引入金属Al,并在高温下原位合成化学稳定性更高、综合性能更优的AlN‑SiC固溶体结合相,制备新型AlN‑SiC固溶体结合SiC复合耐火材料。
Description
技术领域
本发明属于耐火材料领域,尤其涉及一种铝电解槽侧墙用AlN-SiC固溶体结合SiC复合耐火材料及其制备方法。
背景技术
高温熔盐电解法是目前普遍采用的铝电解生产方式。电解槽的寿命以及稳定性一直是工业生产最为关心的课题之一。炭素材料由于价格低廉,一直被用作侧壁内衬材料,但容易被高温的冰晶石电解质侵蚀,造成内衬的破损,而且易被氧化、冲刷,造成侧壁炭块的剥落,严重影响了电解槽寿命。Si3N4-SiC复合材料由于导热性好、耐侵蚀、抗氧化、绝缘性好,有利于电解槽内炉帮的形成,因此现代工业铝电解槽一般采用Si3N4-SiC复合材料作为槽侧部材料。Si3N4-SiC复合材料虽然比炭素材料具有较多的优势,但Si3N4-SiC复合材料在电解槽中使用时,由于受较多因素的综合作用,该复合材料还是会发生一定程度的腐蚀,使用效果不甚理想。
Si3N4-SiC复合材料是通过Si-SiC坯体高温氮化生成,高温下坯体中的Si与N2反应生成Si3N4结合相,将SiC颗粒结合起来,使其具有一定的强度。在铝电解槽应用时,Si3N4结合相是Si3N4-SiC复合材料的薄弱点,SiC相比Si3N4表现出更好的化学稳定性和抗腐蚀能力。在铝电解槽服役过程中:(1)Si3N4易与HF气体发生反应,生成SiF4而被腐蚀;(2)电解温度下,Si3N4亦会与铝液发生反应,生成AlN和Si,而AlN极易水化,会加速材料的腐蚀和损毁;(3)由于铝液中通常还有一定量的钠元素,材料容易发生钠蒸汽渗透作用以及空气和阳极气体的渗透,从而导致Na(g)和Si3N4之间发生化学反应生成Na2SiO3,造成材料的腐蚀。综合以上,铝电解过程中,气体、电解质和铝液均会导致Si3N4不稳定发生转化,导致Si3N4-SiC复合材料失效。
研发一种铝电解槽用高性能SiC基复合材料及其制备方法是本发明亟需解决的问题。
发明内容
为解决现有技术中铝电解槽用Si3N4-SiC复合材料中Si3N4结合相易被腐蚀,化学稳定性较差,导致材料使用性能不佳等不足和缺陷,本发明提供一种新型高性能铝电解槽用AlN-SiC固溶体结合的SiC复合耐火材料及其制备方法。
本发明所采用的技术方案如下。一种AlN-SiC固溶体结合的SiC复合耐火材料,所述复合材料的原料组成按重量百分比计为:碳化硅65%~90%,铝粉5%~20%,硅粉5%~10%,碳粉0~5%,外加结合剂2~5%。
进一步地,所述碳化硅包括粒度为3~0.5mm和0.5~0mm的碳化硅骨料,以及碳化硅细粉,其中粒度为3~0.5mm和0.5~0mm的碳化硅骨料的质量百分比为60%~85%,碳化硅细粉的质量百分比为5~30%。
作为优选,所述结合剂为热固性酚醛树脂结合剂。
本发明还提供了上述AlN-SiC固溶体结合的SiC复合耐火材料的制备方法,步骤如下:将碳化硅、铝粉、硅粉、碳粉和结合剂混合均匀后压制成型,得到低碳Al-Si-SiC复合坯体;
将低碳Al-Si-SiC复合坯体干燥后置于匣钵中,在工业窑炉埋碳条件下进行低温保温,再升温进行高温烧成,使体系中Al、Si、C和CO(g)、N2(g)等各组分之间充分反应,原位合成AlN-SiC固溶体结合相。
作为优选,将低碳Al-Si-SiC复合坯体在150℃~300℃干燥8~24h。
作为优选,所述的在埋碳气氛下低温保温为在500℃~620℃温度范围内保温1~10h,再进一步升温至1450℃~2000℃保温1~24h烧成,升温速率为3~20℃/min。
作为优选,所述窑炉为隧道窑。
在埋碳气氛中500℃~620℃温度范围保温过程中,金属Al粉颗粒表面优先缓慢氮化,生成高熔点的AlN包覆膜,形成Al@AlN包覆结构;随着温度升高至660℃,金属Al熔融,高熔点的AlN包覆层可将Al(l)固定在膜内,防止低温铝液过早地堵塞气孔,阻碍反应的进行;随着温度进一步升高,AlN包覆膜破裂,高活性的Al(l)逸出,裹挟破碎的细小的AlN微粒在结构中迁移并进一步发生反应;高温下,在AlN微粒的诱导作用下,金属Al进一步与N2反应生成高活性的AlN中间体。AlN-SiC固溶体具有和AlN相同的晶体结构,在早期形成的AlN中间体的作用下,AlN-SiC固溶体形成所需的势能大大降低。因此,部分Si、C以原子形式向AlN固溶,进一步生成更加稳定的AlN-SiC固溶体;部分Al(g)、Si(g)、N2(g)和CO(g)在AlN中间体的诱导下直接反应生成AlN-SiC固溶体。当烧成温度高于1700℃时,体系中的SiC细粉进一步参与反应,与AlN固溶生成更加稳定的AlN-SiC固溶体。
本发明技术关键点在于
对比文件《SiC-AlN固溶体结合Al2O3-C复合滑板制备方法》(申请号:CN201910678127.1),以Al2O3、C、Al、Si粉为原料,在1450~1700℃氮气气氛下热处理,通过基质中的Al、Si、C粉和N2之间的化学反应,制得AlN-SiC固溶体结合的Al2O3-C复合滑板。与对比文件相比,本发明具有以下几点优势和创新:(1)与对比文件相比,本发明采用SiC为骨料,热处理温度更高,更有利于AlN-SiC固溶体的合成。SiC是非氧化物耐火材料,具有高熔点(2700℃)、化学性能稳定、导热系数高、热膨胀系数小、耐磨性能好、抗冰晶石侵蚀性能优异等优势。一方面,与Al2O3相比,SiC基体材料可以满足铝电解槽应用需求;另一方面,以SiC为基体,材料可承受的热处理温度更高,更有利于AlN-SiC的合成。(2)对比文件通过在1450~1700℃氮气气氛下热处理,利用Al与氮气、Si和C之间的气-液和固-固反应分别生成AlN和SiC(包括α-SiC、β-SiC)相,其中具有相同晶体结构的AlN和α-SiC(纤锌矿结构)进一步相互固溶,生成AlN-SiC固溶体。然而,固态Si与固态的C反应,在1450~1700℃温度范围内极易生成稳定的β-SiC(立方结构)副产物,影响AlN-SiC固溶体产量,导致材料性能不理想。本发明中,将低碳Al-Si-SiC置于匣钵中高温埋碳气氛下烧成,利用Al和Si与气氛中的N2(g)和CO(g)反应直接生成AlN-SiC固溶体相,具有动力学优势,无副产物。(3)与对比文件中的Al2O3基体相比,本发明中的SiC基体与AlN-SiC固溶体的晶体结构相近,二者的相容性更佳,结合强度更高。同时,本发明中使用的SiC既是基体材料,也是原位合成AlN-SiC固溶体的反应物,从而实现了高强度的反应结合。
有益效果:本发明针对现有铝电解槽用Si3N4-SiC复合材料化学稳定性不佳,使用性能不理想。在铝电解槽服役环境下,Si3N4结合相易与HF气体、Al液、冰晶石等发生化学反应,导致材料结构破坏,使用性能大大降低。本发明以碳化硅、铝粉、硅粉、碳粉为原料制得低碳Al-Si-SiC复合坯体,通过将干燥后的坯体在氮气气氛下500~620℃保温引入Al@AlN包覆结构,提高了金属Al的释放及反应温度,并引入了高活性的AlN中间相作为晶核,在高温下诱导体系中Al、Si、C和CO(g)、N2(g)进一步反应生成相同晶体结构的AlN-SiC固溶体,制得AlN-SiC固溶体结合的SiC复合材料。与Si3N4相比,AlN-SiC固溶体具有优异的化学稳定性和抗侵蚀性能,更适宜应用于铝电解工业,可大大提高铝电解槽用耐火材料的使用寿命。具体表现如下:
(1)在铝电解温度下,现有技术中Si3N4-SiC复合材料中的Si3N4易与Al液发生反应,生成AlN和Si产物,除会污染铝液,AlN的水化还会导致材料粉化、损毁。本发明中AlN-SiC固溶体不与金属铝液反应,且不易被铝液润湿,具有更加优异的抗侵蚀性和化学稳定性,且抗水化性能优异;
(2)在铝电解服役过程中,现有技术中Si3N4-SiC复合材料中的Si3N4结合相还会与冰晶石、含氟蒸气发生化学反应,造成腐蚀和材料损毁。本发明中AlN-SiC固溶体不会与冰晶石、含氟蒸气发生反应,化学稳定性优异,可保持材料结构、性能的稳定,从而实现铝电解槽用耐火材料的长寿化发展。
具体实施方式
实施例1
将70wt.%的碳化硅骨料、5wt.%的碳化硅细粉、10wt.%的铝粉、10wt.%的硅粉和5wt.%的碳粉混合,外加上述混合料3wt.%的酚醛树脂结合剂,混炼均匀,压制成型制得低碳Al-Si-SiC复合材料坯体,并在200℃干燥24小时。将干燥后的低碳Al-Si-SiC复合材料坯体于580℃埋碳气氛下保温4h,再进一步升温至1600℃保温4h烧成,制得AlN-SiC固溶体结合的SiC复合耐火材料。
所得AlN-SiC固溶体结合的SiC复合耐火材料经检测,显气孔率为12.2%,体积密度为2.70g/cm3,常温耐压强度为276MPa。
实施例2
将68wt.%的碳化硅骨料、10wt.%的碳化硅细粉、15wt.%的铝粉、5wt.%的硅粉和2wt.%的碳粉混合,外加上述混合料4wt.%的酚醛树脂结合剂,混炼均匀,压制成型制得低碳Al-Si-SiC复合材料坯体,并在200℃干燥18小时。将干燥后的低碳Al-Si-SiC复合材料坯体于500℃埋碳气氛下保温8h,再进一步升温至1450℃保温8h烧成,制得AlN-SiC固溶体结合的SiC复合耐火材料。
所得AlN-SiC固溶体结合的SiC复合耐火材料经检测,显气孔率为11.7%,体积密度为2.72g/cm3,常温耐压强度为324MPa。
实施例3
将60wt.%的碳化硅骨料、5wt.%的碳化硅细粉、20wt.%的铝粉、10wt.%的硅粉和5wt.%的碳粉混合,外加上述混合料4wt.%的酚醛树脂结合剂,混炼均匀,压制成型制得低碳Al-Si-SiC复合材料坯体,并在200℃干燥12小时。将干燥后的低碳Al-Si-SiC复合材料坯体于580℃埋碳气氛下保温8h,再进一步升温至1700℃保温3h烧成,制得AlN-SiC固溶体结合的SiC复合耐火材料。
所得AlN-SiC固溶体结合的SiC复合耐火材料经检测,显气孔率为13.3%,体积密度为2.71g/cm3,常温耐压强度为378MPa。
实施例4
将85wt.%的碳化硅骨料、5wt.%的碳化硅细粉、5wt.%的铝粉、5wt.%的硅粉混合,外加上述混合料4wt.%的酚醛树脂结合剂,混炼均匀,压制成型制得低碳Al-Si-SiC复合材料坯体,并在300℃干燥10小时。将干燥后的低碳Al-Si-SiC复合材料坯体于620℃埋碳气氛下保温8h,再进一步升温至1800℃保温2h烧成,制得AlN-SiC固溶体结合的SiC复合耐火材料。
所得AlN-SiC固溶体结合的SiC复合耐火材料经检测,显气孔率为14.0%,体积密度为2.70g/cm3,常温耐压强度为233MPa。
实施例5
将72wt.%的碳化硅骨料、3wt.%的碳化硅细粉、20wt.%的铝粉、5wt.%的硅粉混合,外加上述混合料4wt.%的酚醛树脂结合剂,混炼均匀,压制成型制得低碳Al-Si-SiC复合材料坯体,并在150℃干燥24小时。将干燥后的低碳Al-Si-SiC复合材料坯体于600℃埋碳气氛下保温2h,再进一步升温至2000℃保温1h烧成,制得AlN-SiC固溶体结合的SiC复合耐火材料。
所得AlN-SiC固溶体结合的SiC复合耐火材料经检测,显气孔率为13.6%,体积密度为2.73g/cm3,常温耐压强度为293MPa。
Claims (2)
1.一种铝电解槽侧墙用AlN-SiC固溶体结合的SiC复合耐火材料的制备方法,其特征在于,所述材料包括如下质量分数的原料组成:65~90wt%的碳化硅、5~20wt%的铝粉、5~10wt%的硅粉、0~5wt%的碳粉,外加2~5wt%的结合剂,所述结合剂为酚醛树脂;
所述制备方法包括如下步骤:
(1)将碳化硅骨料、碳化硅细粉、铝粉、硅粉、碳粉和结合剂按配比称量,搅拌均匀,制成泥料;
(2)采用压力机将步骤(1)中的泥料压制成坯体,经干燥、烧结工序制得AlN-SiC固溶体结合的SiC复合耐火材料;
步骤(2)中首先将坯体在150~300℃温度范围内干燥10~50小时,将干燥后的坯体置于匣钵中,在隧道窑埋碳条件下于500℃~620℃温度范围内保温1~10h,再以3~20℃/min速率升温至1450℃~2000℃进行原位反应合成,反应合成保温时间为1~24小时。
2.根据权利要求1所述的AlN-SiC固溶体结合的SiC复合耐火材料的制备方法,其特征在于:所述碳化硅包括粒度为3~0.5mm和0.5~0mm的碳化硅骨料,以及碳化硅细粉;其中粒度为3~0.5mm和0.5~0mm的碳化硅骨料的质量百分比为60%~85%,碳化硅细粉的质量百分比为5~30%。
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