WO2022062292A1 - 一种低导热低热膨胀镁基原料及其制备方法 - Google Patents
一种低导热低热膨胀镁基原料及其制备方法 Download PDFInfo
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- the invention belongs to the technical field of refractory materials, and in particular relates to a magnesium-based raw material with low thermal conductivity and low thermal expansion and a preparation method thereof.
- Refractory materials are directly used in high-temperature industrial production processes in various fields of the national economy such as iron and steel, non-ferrous metals, cement, glass, ceramics, chemical industry, machinery, and electric power, and are essential basic materials to ensure the operation and technological development of the above-mentioned industries.
- Magnesia has the advantages of high melting point, high temperature resistance, and good corrosion resistance of alkali high temperature slag. It is one of the most important raw materials in refractory materials. It is widely used in various high temperature industrial refractories. Its service performance and service life It is directly related to the normal operation of the high temperature industry and the quality of the products.
- magnesia has high refractoriness and good corrosion resistance to alkaline high-temperature slag, the thermal conductivity of magnesia is still high, and the defects of poor resistance to high-temperature slag penetration and thermal shock resistance have greatly affected its service life. big restriction.
- the high temperature slag penetration resistance and thermal shock resistance of magnesia are closely related to its microstructure. Therefore, the existing magnesia preparation technologies tend to prepare magnesia raw materials with large and dense grain size, that is, large crystal magnesia.
- the thermal stress is difficult to release due to the small number of grain boundaries, and the thermal shock resistance is usually poor.
- the object of the present invention is to provide a kind of preparation method of low thermal conductivity and low thermal expansion magnesium-based raw material with simple process and easy industrial production, and the concrete processing steps are as follows:
- the mixed powder was mixed by a ball mill at a constant temperature of 25°C for 3 minutes, then placed in a high-temperature furnace for calcination at 250-400°C for 0.5-3 hours, and cooled to room temperature to form the magnesium-based refractory material.
- the particle size of the fused magnesia particles is less than or equal to 1 mm, and the MgO content in the fused magnesia particles is greater than or equal to 96 wt%.
- the particle size of the monoclinic zirconia fine powder is ⁇ 45 ⁇ m, and the ZrO 2 content in the monoclinic zirconia fine powder is ⁇ 98 wt %.
- the particle size of the zirconium oxychloride fine powder is less than or equal to 45 ⁇ m.
- the Ca(OH) 2 of the above-mentioned nano calcium hydroxide powder is ⁇ 98 wt %, and the particle size is ⁇ 0.1 ⁇ m.
- the light-burned magnesium oxide fine powder has MgO ⁇ 95wt% and particle size ⁇ 45 ⁇ m.
- Another aspect of the present invention relates to a magnesium-based refractory material obtained according to the above-mentioned preparation method of a magnesium-based refractory material.
- the present invention has the following positive effects compared with the prior art:
- the invention adopts the millimeter-micron-nanoparticle composite system and the mixing and ball milling processes, combined with the pyrolysis of zirconium oxychloride fine powder and nano-calcium hydroxide powder, and can introduce micro-nano zirconia and oxide around the grain boundary of magnesia. Calcium and make it evenly distributed.
- the zirconia phase transition and the stress generated by the reaction with calcium oxide can well promote the micro-nano zirconia to closely contact the magnesia grain boundary, and its grain boundary impurities CaO in SiO 2 reacts with these active ZrO 2 preferentially to form CaZrO 3 at grain boundaries; an appropriate amount of nano-zirconia ZrO 2 particles are encapsulated in CaO with similar particle size and larger active MgO micropowder particles, which hinders its formation.
- the aggregation reaction with the CaO impurities in the magnesia grain boundary stabilizes the magnesia structure and also plays the role of slow release; these continuously generated appropriate intergranular CaZrO 3 phases can enhance the binding force of the magnesia particles and effectively reduce the magnesia. High thermal conductivity, thermal expansion coefficient and improved slag resistance.
- the invention has the characteristics of simple process and easy industrial production; the prepared magnesium-based raw material with low thermal conductivity and low thermal expansion has the characteristics of low thermal conductivity, low thermal expansion coefficient, good dispersibility and strong slag penetration and erosion resistance.
- the particle size of the fused magnesia particles is less than or equal to 1 mm, and the MgO content in the fused magnesia particles is greater than or equal to 96 wt%.
- the particle size of the monoclinic zirconia fine powder is less than or equal to 45 ⁇ m, and the ZrO 2 in it is greater than or equal to 98wt%,
- the particle size of the zirconium oxychloride fine powder is less than or equal to 45 ⁇ m.
- the Ca(OH) 2 of the nano calcium hydroxide powder is greater than or equal to 98wt%, and the particle size is less than or equal to 0.1 ⁇ m.
- the light-burned magnesium oxide fine powder has MgO ⁇ 95wt% and particle size ⁇ 45 ⁇ m.
- the powder and 0.2wt% maleic acid were mixed uniformly with a high-speed mixer for 15 minutes at a constant temperature of 25 °C to obtain a mixed powder; then the mixed powder was mixed by a ball mill at a constant temperature of 25 °C for 3 minutes, and then It was placed in a high temperature furnace and calcined at 300° C. for 2.5 hours, and cooled to room temperature to obtain the magnesium-based raw material with low thermal conductivity and low thermal expansion of this embodiment.
- Comparative Example 1 Comparative Example 2 Comparative Example 2 Comparative Example 2 Comparative Example 2 Fused magnesia particles 75 20 10 65 35 Monoclinic zirconia fine powder twenty one 50 60 27 45 Zirconium oxychloride fine powder 2 twenty four 30 3 18 Nano calcium hydroxide powder 0.2 4 0 4 0.1 Light Burned Magnesium Oxide Fine Powder 0.8 1 0 1 1.9 maleic acid 1 1 0 0 0 temperature(°C) 300 250 300 350 400 Roasting time (h) 3 2.5 2 2 1.5
- the performance indexes of each embodiment of the present invention and traditional magnesium-based raw materials are compared as shown in Table 2. It can be seen from the above Tables 1 and 2 that 40-60wt% fused magnesia particles and 30-40wt% monoclinic Zirconia fine powder, 5 ⁇ 20wt% zirconium oxychloride fine powder, 0.5 ⁇ 2wt% nano calcium hydroxide powder, 0.2 ⁇ 0.5wt% light burnt magnesia fine powder and 0.1 ⁇ 0.3wt% Malayan
- the acid is mixed with a high-speed mixer for 15 minutes at a constant temperature of 25 °C to obtain a mixed powder.
- the thermal conductivity and thermal expansion coefficient of the final raw material are far lower than those of traditional magnesium-based raw materials.
- the invention adopts the millimeter-micron-nanoparticle composite system and the mixed grinding and ball milling process, combined with the pyrolysis of the zirconium oxychloride fine powder and the nanometer calcium hydroxide powder, and can introduce micro-nano oxide around the magnesia grain boundary.
- Zirconium and calcium oxide are distributed evenly.
- the phase transformation of zirconium oxide and the stress generated by the reaction with calcium oxide can well promote the close contact of micro-nano zirconium oxide with magnesia grain boundaries.
- the CaO in the grain boundary impurities will react preferentially to SiO 2 and these active ZrO 2 to generate CaZrO 3 at the grain boundary; an appropriate amount of nano-ZrO 2 particles are encapsulated in CaO with similar particle size and larger active MgO fine powder particles, which hinders the formation of CaZrO 3 .
- Its aggregation reaction with CaO impurities in magnesia grain boundaries stabilizes the structure of magnesia and also plays a role in slow release; these continuously generated appropriate intergranular CaZrO 3 phases can enhance the binding force of magnesia particles and effectively reduce magnesium Thermal conductivity, thermal expansion coefficient and improved slag resistance of sand.
- the invention has the characteristics of simple process and easy industrial production; the prepared magnesium-based raw material with low thermal conductivity and low thermal expansion has the characteristics of low thermal conductivity, low thermal expansion coefficient, good dispersibility and strong slag penetration and erosion resistance.
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Abstract
一种低导热低热膨胀镁基原料及其制备方法,其技术方案是首先将40~60wt%的电熔镁砂颗粒、30~40wt%的单斜氧化锆细粉、5~20wt%的氧氯化锆细粉、0.5~1.5wt%的纳米氢氧化钙粉体、0.5~1.5wt%的纳米氢氧化钙粉体和0.1~0.3wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将上述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在250~400℃条件下焙烧0.5~3h,最后冷却至室温。该制备方法工艺简单、易于工业化生产,所制备的镁基耐火材料具有较低的导热系数、低热膨胀系数、分散性好和抗熔渣渗透侵蚀能力强的优点。
Description
本发明属于耐火材料技术领域,具体涉及一种低导热低热膨胀镁基原料及其制备方法。
耐火材料直接应用于钢铁、有色、水泥、玻璃、陶瓷和化工、机械、电力等国民经济各个领域的高温工业生产过程中,是保证上述产业运行和技术发展必不可少的基础材料。镁砂具有熔点高、耐高温、抗碱性高温熔渣侵蚀性好等优点,是耐火材料中最重要的原料之一,被广泛应用于各类高温工业用耐火材料,其服役性能和使用寿命直接关系着高温工业的正常运行与产品的品质。
尽管镁砂耐火度高、抗碱性高温熔渣侵蚀性好,但镁砂的导热系数仍然偏高,而且抵御高温熔渣渗透性能和抗热震性能不佳的缺陷对其使用寿命造成了极大的限制。镁砂的抗高温熔渣渗透及抗热震性能与其显微结构有重要联系,熔渣较易通过气孔及晶界渗透进入材料内部从而产生严重的侵蚀。因此,现有镁砂制备技术多倾向于制备晶粒尺寸大且较致密的镁砂原料,即大结晶镁砂。然而,由于氧化镁热膨胀系数较大,大结晶镁砂在遭受温度剧变时,由于晶界数量少,热应力难以得到释放,抗热震性能通常不佳。此外,考虑到现有的镁砂中气孔尺寸通常较大且直接结合程度较低,微孔镁砂的开发有效降低了气孔尺寸,增加了气孔中的闭口气孔比例,能在一定程度上缓解高温熔体的渗透侵蚀,但其轻量多孔化后的隔热性和抗渣性能的平衡性仍然不够优越,有待提高。
发明内容
本发明目的是提供一种工艺简单和易于工业化生产的低导热、低热膨胀镁基原料的制备方法,具体工艺步骤如下:
将40~60wt%的电熔镁砂颗粒、30~40wt%的单斜氧化锆细粉、5~20wt%的氧氯化锆细粉、0.5~2wt%的纳米氢氧化钙粉体、0.2~0.5wt%的轻烧氧化镁细粉和0.1~0.3wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;
然后将所述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在250~400℃条件下焙烧0.5~3h,冷却至室温形成所述镁基耐火材料。
优选地,电熔镁砂颗粒的粒径≤1mm,电熔镁砂颗粒中的MgO含量为≥96wt%。
优选地,单斜氧化锆细粉粒径≤45μm,单斜氧化锆细粉中的ZrO
2含量≥98wt%。
优选地,上述氧氯化锆细粉的粒径≤45μm。
优选地,上述纳米氢氧化钙粉体的Ca(OH)
2≥98wt%,粒径≤0.1μm。
优选地,上述轻烧氧化镁细粉的MgO≥95wt%,粒径≤45μm。
本发明另一方面涉及一种镁基耐火材料,其按照上述镁基耐火材料的制备方法获得。
由于采用上述技术方案,本发明与现有技术相比具有如下积极效果:
本发明采用毫米-微米-纳米颗粒复合体系和混碾及球磨工艺,结合氧氯化锆细粉和纳米氢氧化钙粉体的热解,能在镁砂晶界周围引入微纳米氧化锆和氧化钙并使其均匀分布,该镁基原料在高温使用过程中,氧化锆相变及其与氧化钙反应产生的应力能很好地促进微纳米氧化锆紧密接触镁砂晶界,其晶界杂质中的CaO会优先于SiO
2与这些活性ZrO
2反应在晶界生成CaZrO
3;适量的纳米氧化锆ZrO
2颗粒被包裹具有相似粒径的CaO以及较大的活性MgO微粉粒中,阻碍了其与镁砂晶界中CaO杂质的聚集性反应,稳定了镁砂结构,也起到缓释的作用;这些持续生成的适量晶间CaZrO
3相能增 强镁砂颗粒的结合力,有效降低镁砂的导热系数、热膨胀系数以及提升抗渣性能。
可见,本发明具有工艺简单和易于工业化生产的特点;所制备的低导热低热膨胀镁基原料具有导热系数较低、热膨胀系数低、分散性好和抗熔渣渗透侵蚀能力强的特点。
下面结合具体实施方式对本发明作进一步的描述,并非对其保护范围的限制。
为避免重复,先将本具体实施方式所涉及的物料统一描述如下,实施例中不再赘述:
所述电熔镁砂颗粒的粒径≤1mm,电熔镁砂颗粒中的MgO含量为≥96wt%。
所述单斜氧化锆细粉粒径≤45μm,其中的ZrO
2≥98wt%,
所述氧氯化锆细粉的粒径≤45μm。
所述纳米氢氧化钙粉体的Ca(OH)
2≥98wt%,粒径≤0.1μm。
所述轻烧氧化镁细粉的MgO≥95wt%,粒径≤45μm。
实施例1
将40wt%的电熔镁砂颗粒、40wt%的单斜氧化锆细粉、19wt%的氧氯化锆细粉、0.5wt%的纳米氢氧化钙粉体、0.2wt%的轻烧氧化镁细粉和0.3wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将所述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在250℃条件下焙烧3h,冷却至室温,获得本实施例的低导热低热膨胀镁基原料。
实施例2
将50wt%的电熔镁砂颗粒、35wt%的单斜氧化锆细粉、13wt%的氧氯化锆细粉、1.4wt%的纳米氢氧化钙粉体、0.5wt%的轻烧氧化镁细粉和0.1wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将所述混合粉体经过球磨机在25℃恒温条件下混合 3min,再置于高温炉中在400℃条件下焙烧0.5h,冷却至室温,获得本实施例的低导热低热膨胀镁基原料。
实施例3
将60wt%的电熔镁砂颗粒、33wt%的单斜氧化锆细粉、5wt%的氧氯化锆细粉、1.6wt%的纳米氢氧化钙粉体、0.2wt%的轻烧氧化镁细粉和0.2wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将所述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在300℃条件下焙烧2.5h,冷却至室温,获得本实施例的低导热低热膨胀镁基原料。
实施例4
将52wt%的电熔镁砂颗粒、40wt%的单斜氧化锆细粉、5.2wt%的氧氯化锆细粉、2wt%的纳米氢氧化钙粉体、0.5wt%的轻烧氧化镁细粉和0.3wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将所述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在350℃条件下焙烧2.5h,冷却至室温,获得本实施例的低导热低热膨胀镁基原料。
实施例5
将45wt%的电熔镁砂颗粒、37wt%的单斜氧化锆细粉、16wt%的氧氯化锆细粉、1.5wt%的纳米氢氧化钙粉体、0.3wt%的轻烧氧化镁细粉和0.2wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将所述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在400℃条件下焙烧1.5h,冷却至室温,获得本实施例的低导热低热膨胀镁基原料。
对比例1-5
对比例1-5中,电熔镁砂颗粒、单斜氧化锆细粉、氧氯化锆细粉、纳米氢氧化钙粉体、轻烧氧化镁细粉与马来酸按照表1的重量配比和工艺条件进行。
表1对比例1-5原料配比
对比例1 | 对比例2 | 对比例2 | 对比例2 | 对比例2 | |
电熔镁砂颗粒 | 75 | 20 | 10 | 65 | 35 |
单斜氧化锆细粉 | 21 | 50 | 60 | 27 | 45 |
氧氯化锆细粉 | 2 | 24 | 30 | 3 | 18 |
纳米氢氧化钙粉体 | 0.2 | 4 | 0 | 4 | 0.1 |
轻烧氧化镁细粉 | 0.8 | 1 | 0 | 1 | 1.9 |
马来酸 | 1 | 1 | 0 | 0 | 0 |
温度(℃) | 300 | 250 | 300 | 350 | 400 |
焙烧时间(h) | 3 | 2.5 | 2 | 2 | 1.5 |
表2本发明实施例与对比例1-5原料性能指标对比
本发明的各实施例与传统镁基原料性能指标对比如表2所示,由上述表1和表2可以看出,采用40~60wt%的电熔镁砂颗粒、30~40wt%的单斜氧化锆细粉、5~20wt%的氧氯化锆细粉、0.5~2wt%的纳米氢氧化钙粉体、0.2~0.5wt%的轻烧氧化镁细粉和0.1~0.3wt%的马来酸的在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体,最后获得的原料的导热系数和热膨胀系数均远远低于传统镁基原料。其原因在于本发明采用毫米-微米-纳米颗粒复合体系和混碾及球磨工艺,结合氧氯化锆细粉和纳米氢氧化钙粉体的热解,能在镁砂晶界周围引入微纳米氧化锆和氧化钙并使其均匀分布,该镁基原料在高温使用过程中,氧化锆相变及其与氧化钙反应产生的应力能很好地促进微纳米氧化锆紧密接触镁砂晶界,其晶界杂质中的CaO会优先于SiO
2与这些活性ZrO
2反应在晶界生成CaZrO
3;适量的纳米ZrO
2颗粒被包裹具有相似粒径的CaO以及较大的活性MgO微粉粒中,阻碍了其与镁砂晶界中CaO杂质的聚集性反应,稳定了镁砂结构,也起到缓释的作用;这些持续生成的适量晶间CaZrO
3相能增强镁砂颗粒的结合力,有效降低镁砂的导热系数、热膨胀系数以及提升抗渣性能。
因此,本发明具有工艺简单和易于工业化生产的特点;所制备的低导热低热膨胀镁基原料具有导热系数较低、热膨胀系数低、分散性好和抗熔渣渗透侵蚀能力强的特点。
虽然,上文中已经用一般性说明、具体实施方式,对本发明作了详尽的描述,但在本发明基础上,可以对之作一些修改或改进,这对本领域技术人员而言是显而易见的。因此,在不偏离本发明精神的基础上所做的这些修改或改进,均属于本发明要求保护的范围。
Claims (7)
- 一种低导热低热膨胀镁基原料的制备方法,其特征在于:将40~60wt%的电熔镁砂颗粒、30~40wt%的单斜氧化锆细粉、5~20wt%的氧氯化锆细粉、0.5~2wt%的纳米氢氧化钙粉体、0.2~0.5wt%的轻烧氧化镁细粉和0.1~0.3wt%的马来酸,在25℃恒温条件下采用高速混碾机搅拌15min混合均匀,得到混合粉体;然后将所述混合粉体经过球磨机在25℃恒温条件下混合3min,再置于高温炉中在250~400℃条件下焙烧0.5~3h,冷却至室温形成所述低导热低热膨胀镁基原料。
- 根据权利要求1所述的低导热低热膨胀镁基原料的制备方法,其特征在于所述电熔镁砂颗粒的粒径≤1mm,所述电熔镁砂颗粒中的MgO含量为≥96wt%。
- 根据权利要求1所述的低导热低热膨胀镁基原料的制备方法,其特征在于所述单斜氧化锆细粉粒径≤45μm,所述单斜氧化锆细粉中的ZrO 2含量≥98wt%。
- 根据权利要求1所述的低导热低热膨胀镁基原料的制备方法,其特征在于所述氧氯化锆细粉的粒径≤45μm。
- 根据权利要求1所述的低导热低热膨胀镁基原料的制备方法,其特征在于所述纳米氢氧化钙粉体的Ca(OH) 2≥98wt%,粒径≤0.1μm。
- 根据权利要求1所述的低导热低热膨胀镁基原料的制备方法,其特征在于所述轻烧氧化镁细粉的MgO≥95wt%,粒径≤45μm。
- 一种根据权利要求1-6项中任一项所述的低导热低热膨胀镁基原料的制备方法制得的镁基原料。
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