三氟丙基修饰的二氧化硅膜制备、氢气分离及其水热稳定性能

以三氟丙基三甲氧基硅烷(TFPTMS)和正硅酸乙酯(TEOS)作为前驱体,通过溶胶-凝胶法制备三氟丙基修饰的SiO2膜材料,研究了三氟丙基修饰对膜材料孔结构和疏水性的作用、疏水膜材料的氢气渗透和分离性能以及水热稳定性能。结果表明三氟丙基修饰后的膜材料仍保持良好的微孔结构,孔径狭窄分布在0.45~0.7 nm之间。修饰后膜材料疏水性明显提高,当nTFPTMS/nTEOS=0.6时,对水的接触角达到(102.7°±0.1°)。H2在修饰后膜材料的输运遵循微孔扩散机理,在300℃时,H2的单组份渗透率达到4.77×10-7mol.m-2.s-1.Pa-1,H2/CO2的理想分离系数以及双组份分离系数分别达到6.99和6.93,均高于其Knudsen扩散分离因子。在200℃水蒸气物质的量含量为5%的环境中陈化220 h后,H2的单组份渗透率仅在前3 h有轻微下降,然后基本保持不变,说明三氟丙基修饰的SiO2膜具有良好的水热稳定性。     

十三氟辛基修饰的疏水有机-无机杂化二氧化硅膜孔结构、氢气分离及水热稳定性

采用1,2-双(三乙氧基硅基)乙烷(BTESE)和十三氟辛基三乙氧基硅烷(PFOTES)为前驱体,在酸性条件下通过溶胶-凝胶法制备了十三氟辛基修饰的有机-无机杂化SiO2膜材料。利用接触角测量、红外光谱、动态光散射和N2吸附等测试技术分别对膜材料的疏水性、溶胶粒径和孔结构进行表征,并深入研究有支撑膜材料的氢气渗透、分离性能以及长期水热稳定性。结果表明,十三氟辛基修饰后的膜材料由亲水性变成了疏水性,当nPFOTES/nBTESE=0.6时膜材料对水的接触角达到(110.4±0.4)°,膜材料还保持微孔结构,孔径分布在0.5~0.8 nm。氢气在修饰后的膜材料中的输运遵循微孔扩散机理,在300℃时,氢气的渗透率达到8.5×10-7mol·m-2·s-1·Pa-1,H2/CO2,H2/CO和H2/SF6的理想分离系数分别为5.49,5.90和18.36,均高于相应的Knudsen扩散分离因子。在250℃且水蒸气物质的量分数为5%水热环境下陈化250 h,氢气渗透率和H2/CO2的理想分离系数基本保持不变,膜材料具有良好的水热稳定性。     

苯基修饰的疏水微孔二氧化硅膜的制备与表征

采用苯基三乙氧基硅烷(PTES)和正硅酸乙酯(TEOS)作为前驱体,通过溶胶-凝胶法制备了苯基修饰的SiO2膜材料。利用扫描电镜、N2吸附、视频光学接触角测量仪、热重分析、红外光谱等测试手段对膜的孔结构以及疏水性能进行了表征,最后还研究了修饰后膜材料在室温条件下的单组份气体渗透和分离性能。结果表明,随着PTES加入量的增大,膜材料的疏水性逐渐增强,当PTES/TEOS和H2O/TEOS的化学计量比分别达到0.6和9.6时,膜材料对水的接触角达到115±0.5°,仍保持良好的微孔结构,其孔体积为0.17cm3/g,孔径为0.4-0.5nm。室温下氢气在修饰后SiO2膜的输运既遵循发生在微孔孔道的表面扩散机理也遵循发生在较大孔道或者微缺陷的努森扩散机理,膜材料的H2渗透率达到1.49×10-6mol?m-2?Pa-1?s-1,H2/CO2 和H2/SF6的理想分离系数分别达到4.64和365.59     

表面修饰的有机-无机杂化微孔SiO2膜的制备及氢气分离性能

采用苯基三乙氧基硅烷(PTES)和1,2-双(三乙氧基硅基)乙烷(BTESE)为前驱体, 通过溶胶-凝胶法制备了苯基修饰的有机-无机杂化SiO2 膜材料. 通过N2吸附、视频光学接触角测量、热重分析和红外光谱对膜材料的孔结构和疏水性能进行了表征, 并深入研究了膜材料的氢气渗透和分离性能. 结果表明, 修饰后的膜材料具有微孔结构, 孔径集中分布在0.4~0.6 nm. 在温度为40 ℃, 湿度为70%~80%的水热环境下陈化30 d后, 膜材料仍保持微孔结构. 苯基修饰后膜材料具有疏水性, 当n(PTES)/n(BTESE)=0.6时, 膜材料对水的接触角达到(125±0.4)°. 氢气在膜材料中的输运遵循活化扩散机理, 300 ℃时, 膜材料的H2渗透率达到8.71×10-7mol·m-2·Pa-1·s-1, H2/CO2的理想分离系数达到5.53.     

三氟丙基修饰的二氧化硅膜制备、氢气分离及其水热稳定性能

以三氟丙基三甲氧基硅烷(TFPTMS)和正硅酸乙酯(TEOS)作为前驱体,通过溶胶-凝胶法制备三氟丙基修饰的SiO₂膜材料,研究了三氟丙基修饰对膜材料孔结构和疏水性的作用、疏水膜材料的氢气渗透和分离性能以及水热稳定性能。结果表明三氟丙基修饰后的膜材料仍保持良好的微孔结构,孔径狭窄分布在0.45~0.7 nm之间。修饰后膜材料疏水性明显提高,当n_TFPTMS/n_TEOS=0.6时,对水的接触角达到(102.7°±0.1°)。H₂在修饰后膜材料的输运遵循微孔扩散机理,在300 ℃时,H₂的单组份渗透率达到4.77×10^-7 mol·m^-2·s^-1·Pa^-1,H₂/CO₂的理想分离系数以及双组份分离系数分别达到6.99和6.93,均高于其Knudsen扩散分离因子。在200 ℃水蒸气物质的量含量为5%的环境中陈化220 h后,H₂的单组份渗透率仅在前3 h有轻微下降,然后基本保持不变,说明三氟丙基修饰的SiO₂膜具有良好的水热稳定性。     

三氟丙基修饰的有机-无机杂化二氧化硅膜制备、氢气分离及水热稳定性能

以三氟丙基三甲氧基硅烷(TFPTMS)和1,2-双(三乙氧基硅基)乙烷(BTESE)为前驱体, 通过溶胶-凝胶法在酸性条件下制备三氟丙基修饰的有机-无机杂化SiO₂膜材料, 并深入研究三氟丙基修饰对溶胶粒径和疏水性能的影响以及膜材料的氢气渗透分离性能和长期水热稳定性. 结果表明三氟丙基已成功修饰到有机-无机杂化SiO₂膜材料中, 且随着TFPTMS修饰量的增加, 溶胶粒径有减小趋势, 膜材料的疏水性能逐渐提高. 当n(TFPTMS)/n(BTESE)＝0.6时, 溶胶平均粒径为2.11 nm, 膜材料对水的接触角达到111.6°±0.7°. H₂在修饰后膜材料中的输运主要遵循微孔扩散机理, 300 ℃时H₂的渗透率为8.86×10^-7 mol·m^-2·s^-1·Pa^-1, H₂/CO₂的理想分离系数达到5.4, 且当进气摩尔比例为1∶1时H₂/CO₂的双组分气体分离系数达到了4.82, 均高于Knudsen扩散分离因子(H₂/CO₂＝4.69), 膜材料呈现出良好的分子筛分性能. 膜材料在250 ℃及水蒸气摩尔含量为5%的水热环境中能稳定工作300 h以上.     

十三氟辛基修饰的疏水有机-无机杂化二氧化硅膜孔结构、氢气分离及水热稳定性

采用1,2-双（三乙氧基硅基）乙烷（BTESE）和十三氟辛基三乙氧基硅烷（PFOTES）为前驱体,在酸性条件下通过溶胶-凝胶法制备了十三氟辛基修饰的有机-无机杂化SiO₂膜材料。利用接触角测量、红外光谱、动态光散射和N₂吸附等测试技术分别对膜材料的疏水性、溶胶粒径和孔结构进行表征,并深入研究有支撑膜材料的氢气渗透、分离性能以及长期水热稳定性。结果表明,十三氟辛基修饰后的膜材料由亲水性变成了疏水性,当n_PFOTES/n_BTESE=0.6时膜材料对水的接触角达到（110.4±0.4）°,膜材料还保持微孔结构,孔径分布在0.5~0.8nm。氢气在修饰后的膜材料中的输运遵循微孔扩散机理,在300℃时,氢气的渗透率达到8.5×10^-7mol·m^-2·s^-1·Pa^-1,H₂/CO₂,H₂/CO和H₂/SF₆的理想分离系数分别为5.49,5.90和18.36,均高于相应的Knudsen扩散分离因子。在250℃且水蒸气物质的量分数为5%水热环境下陈化250h,氢气渗透率和H₂/CO₂的理想分离系数基本保持不变,膜材料具有良好的水热稳定性。     

Pd修饰的选择分离氢的负载型PI-SiO2杂化膜的制备及应用

 以负载TiO2过渡层的硅藻土-莫来石陶瓷膜管为支撑体,采用溶胶-凝胶法制备了金属钯修饰的负载型聚酰亚胺-二氧化硅杂化膜(Pd-PI-SiO2). 利用红外光谱、扫描电子显微镜和低温N2吸附等手段对膜材料结构、微观形貌及孔径分布等进行了表征,并对CH4, H2O, H2, CO2, CO和N2等气体进行了选择渗透性测试. 结果表明,杂化膜中聚酰亚胺与二氧化硅间形成了键联结构; 钯以还原后的金属态存在且分散均匀,能对聚酰亚胺-二氧化硅膜的孔结构起到修饰作用; 杂化膜孔径为 4 nm 左右; N2在此膜中的渗透通量为0.20×10-7 mol/(m2·Pa·s), H2/N2分离因子达542; 钯能够促使H2在膜渗透过程中按表面扩散机制进行,有助于分离混合气中的氢分子.     

溶胶凝胶法合成聚酰亚胺二氧化钛杂化膜

溶胶凝胶法制备了负载型聚酰亚胺 二氧化钛杂化膜 ,采用扫描电镜、红外光谱、TG DTA、压汞法和气体渗透性能测试装置对膜材料的表面形貌、表面结构、热性能、孔径分布和气体渗透性能进行了表征 .结果表明 ,杂化膜材料形成了有机相包裹无机相的交联结构 ;聚酰亚胺与二氧化钛粒子形成了新型键联结构 ;其热分解温度随二氧化钛含量的增加而降低 ,在 4 5 0℃以下热稳定性优于聚酰亚胺膜材料 ;平均孔径随二氧化钛含量增大而增大 ,孔径分布趋于弥散 ;N2 、H2 和CO2 在膜内渗透由Knudsen扩散控制 ,H2 O N2 分离因子均大于Knudsen扩散值 ,表现出良好的亲水性 .     

聚酰亚胺-二氧化硅杂化膜的制备及表征

 采用溶胶－凝胶法制备了两类具有不同二氧化硅含量的聚酰亚胺－二氧化硅（PI－SiO2）杂化膜,并用SEM,IR,TG－DTA,氮吸附和气体渗透性能测试等手段对该膜材料的表面形貌、结构、热性能、孔径分布和气体渗透性能进行了表征．结果表明,PI－SiO2膜材料中SiO2粒子的分散良好,与有机相之间存在着分相和键联;膜材料的玻璃化温度θg均随SiO2含量的增加而升高．相比之下,在酸性条件下制备的T系列杂化膜比在碱性条件下合成的S系列杂化膜对θg的影响更大一些;杂化膜具有较好的气体渗透性能和亲水性能,其H2O／N2和H2O／CH4的分离系数远大于努森扩散的理论值．     

中空纤维担载氧化硅膜的制备及结构研究

采用SXRD,HRTEM,FTIR,SEM和氮气吸附等测试手段对膜结构、形貌、孔径及其分布进行了表征.SXRD和HRTEM结果显示,所制备的膜具有短程有序结构.SEM分析发现膜表面完整.气体渗透实验表明,担载膜具有一定的气体选择性,在0.1MPa下对H₂/N₂和CH₄/N₂的分离因子分别为2.25和1.56,气体透过膜孔的扩散由努森机制所控制.等温氮气吸附实验显示,经500℃热处理后氧化硅膜的最可几孔径小于3.34nm,非担载膜的比表面积为919.8m²/g,孔容为0.43mL/g.     

Fundamentals of melt infiltration for the preparation of supported metal catalysts. The case of Co/SiO2 for Fischer-Tropsch synthesis

We explored melt infiltration of mesoporous silica supports to prepare supported metal catalysts with high loadings and controllable particle sizes. Melting of Co(NO(3))(2)·6H(2)O in the presence of silica supports was studied in situ with differential scanning calorimetry. The melting point depression of the intraporous phase was used to quantify the degree of pore loading after infiltration. Maximum pore-fillings corresponded to 70-80% of filled pore volume, if the intraporous phase was considered to be crystalline Co(NO(3))(2)·6H(2)O. However, diffraction was absent in XRD both from the ordered mesopores at low scattering angles and from crystalline cobalt nitrate phases at high angles. Hence, an amorphous, lower density, intraporous Co(NO(3))(2)·6H(2)O phase was proposed to fill the pores completely. Equilibration at 60 °C in a closed vessel was essential for successful melt infiltration. In an open crucible, dehydration of the precursor prior to infiltration inhibited homogeneous filling of support particles. The dispersion and distribution of Co(3)O(4) after calcination could be controlled using the same toolbox as for preparation via solution impregnation: confinement and the calcination gas atmosphere. Using ordered mesoporous silica supports as well as an industrial silica gel support, catalysts with Co metal loadings in the range of 10-22 wt % were prepared. The Co(3)O(4) crystallite sizes ranged from 4 to 10 nm and scaled with the support pore diameters. By calcination in N(2), pluglike nanoparticles were obtained that formed aggregates over several pore widths, while calcination in 1% NO/N(2) led to the formation of smaller individual nanoparticles. After reduction, the Co/SiO(2) catalysts showed high activity for the Fischer-Tropsch synthesis, illustrating the applicability of melt infiltration for supported catalyst preparation.     

Pore Modification in Porous Ceramic Membranes With Sol-Gel Process and Determination of Gas Permeability and Selectivity

Summary: The aim of the study was to investigate the variation in total surface area, porosity, pore size, Knudsen and surface diffusion coefficients, gas permeability and selectivity before and after the application of sol-gel process to porous ceramic membrane in order to determine the effect of pore modification. In this study, three different sol-gel process were applied to the ceramic support separately; one was the silica sol-gel process which was applied to increase porosity, others were silica-sol dip coating and silica-sol processing methods which were applied to decrease pore size. As a result of this, total surface area, pore size and porosity of ceramic support and membranes were determined by using BET instrument. In addition to this, Knudsen and surface diffusion coefficients were also calculated. After then, ceramic support and membranes were exposed to gas permeation experiments by using the CO₂ gas with different flow rates. Gas permeability and selectivity of those membranes were measured according to the data obtained. Thus, pore surface area, porosity, pore size and Knudsen diffusion coefficient of membrane treated with silica sol-gel process increased while total surface area was decreasing. Therefore, permeability of ceramic support and membrane treated with silica sol-gel process increased, and selectivity decreased with increasing the gas flow rate. Also, surface area, porosity, pore size, permeability, selectivity, Knudsen and surface diffusion coefficients of membranes treated with silica-sol dip coating and silica-sol processing methods were determined. As a result of this, porosity, pore size, Knudsen and surface diffusion coefficients decreased, total surface area increased in both methods. However, viscous flow and Knudsen flow permeability were detected as a consequence of gas permeability test and Knudsen flow was found to be a dominant transport mechanism in addition to surface diffusive flow owing to the small pore diameter in both methods. It was observed that silica-sol processing method had lower pore diameter and higher surface diffusion coefficient than silica-sol dip coating method.     

十七氟癸基修饰的有机-无机杂化二氧化硅膜材料的制备及气体分离性能

以十七氟癸基三乙氧基硅烷(PFDTES)和1,2-双(三乙氧基硅基)乙烷(BTESE)为前驱体, 通过溶胶-凝胶法制备了十七氟癸基修饰的SiO₂溶胶, 采用浸渍提拉法在γ-Al₂O₃/α-Al₂O₃多孔陶瓷支撑体上涂膜, 然后在N₂气氛保护下烧结成完整无缺陷的有机-无机杂化SiO₂膜. 利用扫描电子显微镜对膜材料的形貌进行观察, 通过动态光散射技术对溶胶粒径及分布进行测试, 利用视频光学接触角测量仪、 红外光谱仪和热分析仪表征了十七氟癸基修饰对有机-无机杂化SiO₂膜疏水性的影响. 结果表明, 十七氟癸基已经成功修饰到SiO₂膜材料中, 且随着PFDTES加入量的增大, 溶胶粒径和膜材料对水的接触角不断增大. 当n(PFDTES): n(BTESE)=0.25: 1时, 溶胶粒径分布较窄, 平均粒径为3.69 nm, 膜材料对水的接触角为(112.0±0.4)º. 在修饰后的有机-无机杂化SiO₂膜中H₂的输运遵循微孔扩散机理, 在300℃时, H₂的渗透率达到5.99×10^-7 mol·m^-2·Pa^-1·s^-1, H₂/CO和H₂/CO₂的理想分离系数分别达到9.54和5.20, 均高于Knudsen扩散的理想分离因子, 表明膜材料具有良好的分子筛分效应.     

疏水介孔二氧化硅膜的制备与表征

用甲基三乙氧基硅烷(MTES)代替部分正硅酸乙酯(TEOS)作为前驱体，以聚乙烯醚-聚丙烯醚-聚乙烯醚三嵌段共聚物(P123)作有机模板剂，通过共水解缩聚反应制备了甲基修饰的介孔SiO₂膜。利用N₂吸附、FTIR、²⁹Si MAS NMR以及接触角测量仪对膜的孔结构和疏水性进行了表征。结果表明，修饰后的膜材料具有良好的介孔结构，最可几孔径为4.65 nm，孔体积为0.69 cm³·g^-1，比表面积为938.4 m²·g^-1；同时疏水性明显提高，当n_MTES/n_TEOS达到1.0时，其对水的接触角达到109°± 1.1°。气体渗透实验表明气体通过膜孔的扩散由努森机制所控制。     

Sol–gel derived mesoporous and microporous alumina membranes

Stable polymeric and colloidal boehmite sols were prepared by sol–gel process through controlled hydrolysis/condensation reactions. The particle sizes of the colloidal sols were in the 12–25 nm range depending on the process parameters and about 2 nm for polymeric sols. The presence of a significant increase in the microporosity content of the heat treated polymeric membranes relative to the mesoporous colloidal membranes might make the design of thermally stable microporous alumina membranes with controlled pore structures possible. The phase structure evolution in the 600–800 °C range had shown that the crystallization of the gamma alumina in the amorphous matrix starts at about 800 °C. This indicated that the pore structure stability may be enhanced through processing up to this relatively high temperature in polymeric alumina derived unsupported membranes. The permeance values of the two and three layered colloidal alumina membranes were observed to be independent of pressure which implies that the dominant gas transport mechanism is Knudsen diffusion in these structures. This was also supported by the 2.8 nm BJH pore sizes of the colloidal membranes. The Knudsen diffusion equation derived permeances of the polymeric alumina membranes with thicknesses of about 300 nm were determined to be very close to the experimentally determined permeance values.     

Microporous silica membranes deposited on porous supports by filtration

Water based particulate silica sols have been coated onto Anodisc® filters by filtration. The membranes prepared by this technique are more uniform than those formed by slip-casting. The average diameter of the silica particles used in these studies is 6 nm. Unsupported silica membranes formed from these sols have a microporous structure. The adhesion between silica and the alumina support is influenced by the sol pH. Coating thickness can be controlled by the concentration and volume of the sol filtered. Polyvinyl alcohol (PVA) was used to improve adhesion and to prevent cracking during drying. When the PVA/SiO₂ ratio by weight is less than 20%, the membranes retain their microporosity after firing. The membranes prepared by this filtration method have their pore size in Knudsen diffusion range.     

不同铈添加量对CeO2-ZrO2-Al2O3材料性能的影响

采用共沉淀法制备了一系列不同铈添加量的CeO2-ZrO2-Al2O3(CZA)储氧材料,并通过XRD、低温N2吸附-脱附、氧脉冲吸附(OSC)和H2-TPR等手段进行了表征。XRD结果表明,在1 000和1 100℃高温焙烧后,当CeO2添加量为8%时样品具有最好的结构稳定性能。N2吸附-脱附结果表明,CeO2添加量为8%时样品具有最好的织构性能,1 000℃时,比表面积和孔容分别为:136.6 m2.g-1和0.38 mL.g-1;1 100℃时,比表面积和孔容分别为:83.7 m2.g-1和0.23 mL.g-1。OSC结果显示,CeO2添加量为8%时样品具有最大的储氧量,1 000℃和1 100℃分别为70μmol.g-1和31μmol.g-1。H2-TPR结果表明,CeO2添加量为8%时样品具有最佳的还原性能。