新型电解质材料CaZr_(0.1)Ti_(0.9)O_3的制备与电性能

采用溶胶-燃烧法合成了可用于固体氧化物燃料电池(SOFC)的新型固体电解质材料CaZr_(0.1)Ti_(0.9)O_3.通过XRD、交流复阻抗等电化学方法对样品的结构、电导性能进行了表征,并考察了材料的烧结性能. 结果表明,溶胶-燃烧法可以成功制备出具有良好烧结性能的CaZr_(0.1)Ti_(0.9)O_3电解质粉末,1 400 ℃下得到的烧结体的相对密度可达到95%. 电性能测试表明,CaZr_(0.1)Ti_(0.9)O_3烧结体在中温范围内具有较高的氧离子电导率(σ_(800 ℃)＝2.24×10~(-3)S/cm)、低的电导活化能(0.89 eV).     

Ce1-xGdxO2-x/2的溶胶-凝胶法合成及其性质

利用溶胶-凝胶法合成了Ce₁-xGdxO_2-x/2(x=0.1～0.6)系列固体电解质,系统地研究了其结构、热膨胀系数和导电性.XRD结果表明,160℃即完全形成立方萤石结构.由于溶胶-凝胶法合成的物质粒度均匀,颗粒小,故在较低温度(1300℃)时即可形成高致密样品,此温度明显低于传统的高温固相法烧结温度(1600～1650℃).高温X射线衍射测得Ce_0.8Gd_0.2O_1.9的热膨胀系数为8.125×10^-6K₁.阻抗谱表明,溶胶-凝胶法合成可减少或消除固体电解质的晶界电阻,600℃时Ce_0.8Gd_0.2O_1.9的电导率为5.26×10^-3S/cm,活化能E_a=0.82eV.     

溶胶-凝胶法制备(Ba0.85Ca0.15)(Ti0.9Zr0.1)O3无铅压电陶瓷研究

锆钛酸钡钙基无铅压电陶瓷由于具有较好的压铁电性能且环境友好而备受研究者关注,但其存在烧结温度高(>1450℃)、居里温度低等缺点。为降低锆钛酸钡钙基压电陶瓷的预烧及烧结温度,并优化其电学性能,本研究采用溶胶-凝胶法成功合成了(Ba_0.85Ca_0.15)(Ti_0.9Zr_0.1)O₃无铅压电陶瓷的前驱粉体,并在预烧温度为1000℃、烧结温度为1420℃时成功制备了(Ba_0.85Ca_0.15)(Ti_0.9Zr_0.1)O₃陶瓷,相较于传统固相法,陶瓷的预烧温度降低了250℃,烧结温度降低了30℃,成功改善了陶瓷的烧结行为,得到了铁电性能、介电性能和压电性能优良且致密性良好的低温烧结陶瓷。     

Al2O3负载Pt催化剂的合成及其甲醇低温催化燃烧性能研究

采用一步合成法制备了Al₂O₃负载Pt催化剂Pt/Al₂O₃,以甲醇催化燃烧作为目标反应研究了其催化性能,考察了还原剂浓度、表面活性剂用量、表面活性剂浓度和煅烧温度对Pt/Al₂O₃甲醇低温催化燃烧性能的影响。结果表明,当还原剂浓度为0.1 mol/L、表面活性剂(CTAB)用量为8.53 g/g_cat.、表面活性剂浓度为0.1 mol/L、煅烧温度为600℃时,所得催化剂的活性最高,25℃下甲醇催化燃烧的转化率达到52%。而改进一步合成法制备的负载型催化剂Pt/Al₂O₃具有更高的甲醇催化燃烧活性,25℃下甲醇催化燃烧的转化率为84%。     

Sn0.5Ti((0.5)O2固溶体的溶胶-凝胶法制备、表征及其热稳定性研究

采用溶胶-凝胶法制备了Sn_0.5Ti_0.5O₂固溶体.用X射线衍射(XRD)、差热分析(DTA)和红外(IR)技术对材料的结构和热稳定性进行了分析表征.固溶体的热稳定性与起始反应温度有关,在40℃水浴温度下制备的凝胶经1000℃烧结,发生了相分解,出现了富Sn和富Ti相,而在80℃水浴温度下制备的凝胶经1200℃烧结也不发生相分解,仍以Sn_0.5Ti_0.5O₂相存在,而且用差热分析也得到了同样的结论.     

纳米晶材料SrMgxTi1-xO3的合成与表征

采用硬脂酸法合成纳米晶SrMg_xTi_1-xO₃(x=0.1～0.5)材料.用DTA,TG,XRD,IR,XPS和TEM进行表征.结果表明,粉末粒径d随SrMg_xTi_1-xO₃中镁含量、烧结温度和烧结时间的改变而变化;烧结所产生的粉末粒度分布均匀、大小适中;Mg²⁺部分替代SrTiO₃的Ti⁴⁺后,O的1_s光谱随着Mg²⁺含量的不同而发生变化.     

Fe2O3/Al2O3氧载体制备方法的研究

采用溶胶-凝胶法、共沉淀法、水热合成法、低热固相合成法、机械混合法、燃烧合成法和冷冻成粒法制备铁基氧载体Fe₂O₃/Al₂O₃,并通过物理和化学表征手段来筛选和优化制备方法和制备工艺。对煅烧后的氧载体进行硬度测试,结果表明,溶胶-凝胶法、共沉淀法、机械混合法、燃烧合成法和冷冻成粒法制备的氧载体硬度较高;载体的X射线衍射(XRD)谱图表明,各种制备方法均能制得物相组成为Fe₂O₃/Al₂O₃的氧载体,且随着煅烧温度的提高、煅烧时间的延长,氧载体的结晶度、晶体粒径逐渐增大,煅烧温度1 200℃的氧载体的机械性能、晶体结构、晶相组成更稳定。借助化学吸附仪的程序升温还原(TPR)实验表征氧载体的反应活性,并计算氧载体活性度。综合物理和化学表征实验结果表明,最优制备方法为溶胶-凝胶法和冷冻成粒法。     

新型导电陶瓷Sm0.9Sr0.1Al0.5Mn0.5O3-δ的制备及其电性能研究

采用有机凝胶法结合固相烧结技术制备了Sm0.9Sr0.1Al0.5Mn0.5O3－δ (SSAM9155)新型导电陶瓷. 通过TG/DTA, FTIR, XRD, SEM和直流四引线法系统研究了凝胶前驱体的热分解及其相转化过程和烧结体的结构、相稳定性、微观形貌、电导率以及电输运机制. 结果表明, 凝胶前驱体在900 ℃焙烧5 h可以形成完全晶化的四方钙钛矿相纳米粉体; 高温烧结制得的SSAM9155陶瓷的电导率取决于p型电导, 电导率随温度的升高而增大, 导电行为符合p型小极化子跳跃机制; 随烧结温度的升高或保温时间的延长, SSAM9155陶瓷的电导率和相对密度都先增大后减小, 1600 ℃烧结10 h制得的SSAM9155陶瓷具有最高的电导率和相对密度(98%), 该样品在空气和氢气气氛中850 ℃时的电导率分别为8.21和1.26 S•cm－1, 表观活化能分别为0.265和0.465 eV. 具有较高电导率的Sr, Mn掺杂的SmAlO3导电陶瓷有望成为一种新型的固体氧化物燃料电池(SOFC)阳极材料.     

BaCe0.5Zr0.4Y0.1O3-α的溶胶-凝胶法制备及其电性能

采用溶胶-凝胶法, 以低于固相合成法150～250 ℃的温度进行烧结, 分别制备了BaCe0.9Y0.1O3-α和BaCe0.5Zr0.4Y0.1O3-α固体电解质. 应用AUTOLAB PGSTA 30型电化学工作站测定了两种电解质在不同温度下的阻抗谱, 在350～800 ℃范围内电导率分别为1.62×10-4～6.43×10-3 S·cm-1, 2.52×10-5～3.73×10-3 S·cm-1, 电导激活能分别为0.54和0.84 eV. 同时用高温固相合成法合成了BaCe0.9Y0.1O3-α质子导体, 在相同条件下其电导率为1×10-4～4×10-3 S·cm-1, 激活能为0.50 eV. 实验结果表明 用溶胶-凝胶法得到的材料在烧结温度低于固相合成法150～250 ℃的情况下, 制备出的样品电导率高;对于同一质子导体BaCe0.9Y0.1O3-α, 用Zr代替部分Ce, 固体电解质的电导率明显降低.     

SrFe0.6Cu0.3Ti0.1O3-δ混合导体透氧材料的稳定性

利用柠檬酸络合法制备了SrFe(Cu,Ti)O_3-δ混合导体透氧材料。 采用XRD、O₂-TPD、H₂-TPR、SEM等测试技术考察了材料的稳定性。 结果表明,SrFe_0.7Cu_0.3O_3-δ在低氧压下会发生相分解,产生SrCuO₂杂相,而掺杂Ti后的SrFe_0.6Cu_0.3Ti_0.1O_3-δ在低氧压下保持单一的钙钛矿结构。 H₂-TPR和O₂-TPD的测试表明,Ti⁴⁺的掺杂提高了材料的氧脱附起始温度和其它金属离子的还原温度。 SrFe_0.6Cu_0.3Ti_0.1O_3-δ膜在透氧过程中,会有Cu²⁺和Sr²⁺从钙钛矿结构中析出,在原晶粒边界形成新的小晶粒,但这种轻微的组分偏析没有影响到材料的透氧量,此透氧膜在66 h的操作过程中显示了良好的稳定性。     

EDTA-甘氨酸法制备SmBaCo2O5+δ阴极材料及其性能

采用EDTA-甘氨酸法(EGP)合成了中温固体氧化物燃料电池(IT-SOFC)的阴极材料SmBaCo2O5+δ(SBCO).通过热重-差热分析(TG-DTA),X射线衍射(XRD),透射电镜(TEM),扫描电镜(SEM),直流四极法及交流阻抗技术分析材料的性能.结果表明,初始粉体在850°C煅烧5 h形成钙钛矿结构单相.EGP制备的SBCO粉体颗粒细小、分散性好、粒径分布均匀,其与Sm0.2Ce0.8O1.9(SDC)电解质材料具有良好的高温化学相容性.SBCO的电导率在500-800°C时达到668-382 S cm-1.以SDC为电解质,SBCO为阴极制备对称半电池,其界面结合良好,颗粒连接充分,形成好的三相界面,具有高的阴极催化活性,750°C时阴极极化电阻为0.0688Ωcm2,远低于固相法(SSR)的值,活化能(Ea)为122.21 kJ mol-1.     

一种具有低SO2氧化活性并满足欧V排放标准的柴油车氧化型催化剂

制备了具有高性能的稀土储氧材料Ce_0.75Zr_0.25O₂-Al₂O₃,Ti_0.9Zr_0.1O₂复合材料和Cr改性的β分子筛(Cr-β分子筛),并以此制备了单Pt型柴油车尾气净化氧化型催化剂.低温N₂吸附-脱附、储氧量测试结果表明,Ce_0.75Zr_0.25O₂-Al₂O₃样品具有较大的比表面积和优异的储氧性能,Ti_0.9Zr_0.1O₂复合材料也具有优越的织构性能.催化剂对HC和CO具有较高的催化活性,可使SOF在140℃开始转化,且具有较低的SO₂氧化活性.在YC4F国Ⅳ柴油机的测试结果表明,经该催化剂处理后的尾气排放能够满足欧Ⅴ排放标准对HC和CO排放要求.     

Impedance Study of the Conductivity of Solid Oxide Electrolyte Films SrZr<Subscript>0.95</Subscript>Y<Subscript>0.05</Subscript>O<Subscript>3–δ</Subscript> and CaZr<Subscript>0.9</Subscript>Y<Subscript>0.1</Subscript>O<Subscript>3–δ</Subscript>

Information on the across-plane conductivity of films of solid-oxide electrolytes SrZr_0.95Y_0.05O_3–δ and CaZr_0.9Y_0.1O_3–δ deposited on ion-conducting supports is acquired by the impedance method. It is shown that the support/film interface and the intergrain boundaries considerably affect the across-plane charge transfer in the film. The effect of the crystallographic orientation of the YSZ support on the microstructure and conductivity of the CaZr_0.9Y_0.1O_3–δ electrolyte film is demonstrated.     

Chemical synthesis and granulometric composition of CaZr<Subscript>0.9</Subscript>Y<Subscript>0.1</Subscript>O<Subscript>3–δ</Subscript> powders

CaZr_0.9Y_0.1O_3–δ powders were synthesized by chemical solution methods: modified Pechini method and from solutions of inorganic salts in water and ethanol. The structure crystallizes into the orthorhombic type upon annealing at 1000°C for powders prepared by the Pechini method and from solution of salts in water. It was shown that CaZr_0.9Y_0.1O_3–δ powders synthesized by various methods have different dispersities. The results obtained in a study of the granulometric composition by the sedimentation method and microscopic analysis enable fabrication of dense and mechanically strong electrolyte films and ceramics.     

Ceramic electrolytes based on (Ba1 − x Ca x )(Zr0.9Y0.1)O3 solid solution

The aim of this work was to study the electrical and electrochemical properties of the (Ba_1???x Ca _x )(Zr_0.9Y_0.1)O₃ solid solutions. The powders of different calcium content (x?=?0, 0.05, 0.1, and 1) were prepared by a thermal decomposition of organo-metallic precursors containing ethylenediaminetetraacetate acid. X-ray diffraction analysis showed that a small substitution of calcium for barium caused formation of cubic solid solutions with the decreasing cell parameters. Electrical conductivity measurements were performed by the d.c. four-probe method in controlled gas atmospheres containing Ar, air, H₂, and/or H₂O at temperature from 300 to 800 °C. It was found that the conductivity depended on a chemical composition of the samples and the atmosphere. Overall, the electrical conductivity was higher in wet atmospheres that contained oxygen that was in accordance with the model of a proton transport in perovskite structure which assumed the presence of the oxygen vacancies. The solid solution containing 5 mol% of calcium showed the highest conductivity and the lowest activation energy of conductivity regardless of the atmospheres; this can be attributed to the local changes in the cubic perovskite structure. Test results for CaZr_0.9Y_0.1O₃ used as an electrolyte in solid oxide galvanic cells involving CaCr₂O₄ as a reference electrode are also reported.     

Structure, Microstructure, and Mixed Conduction of [(ZrO2)0.92(Y2O3)0.08]0.9(TiO2)0.1

[(ZrO₂)_0.92(Y₂O₃)_0.08]_0.9(TiO₂)_0.1 (titania-doped yttria stabilized circonia, 10TiYSZ) samples were prepared by solid state reaction from mixtures of 8 mol% yttria-doped ZrO₂ (YSZ) and TiO₂ and characterized in terms of structure, microstructure, and electrical properties. [(ZrO₂)_0.97(Y₂O₃)_0.03]_0.9(TiO₂)_0.1 (titania-doped tetragonal zirconia polycrystalline, 10TiTZP) was also prepared for comparison in some specific studies. Ionic transport properties were measured by impedance spectroscopy in air as a function of temperature. DC techniques including electromotive force (EMF) and Ion Blocking measurements (IB) were carried out in order to determine the electronic contribution to the total conductivity. The addition of titania to YSZ induces the tetragonal zirconia phase formation, thus [(ZrO₂)_0.92(Y₂O₃)_0.08]_0.9(TiO₂)_0.1 is a composite material and is constituted by two solid solutions, titania-doped yttria-stabilized zirconia (67.7 mole fraction) and titania-doped tetragonal zirconia (32.3 mole fraction). A decrease in bulk ionic conductivity, of one order of magnitude, when TiO₂ is added to YSZ is observed in the whole temperature range. Furthermore, in the bulk conductivity vs the reciprocal of the temperature plot, a bending (from 550°C to higher temperatures) toward higher activation energies was detected. The bending could indicate the existence mainly of Ti⁴⁺-Vö associated pairs with an association energy of 0.43±0.02 eV. It could mean that Ti-O bonds become stronger and shorter and could produce the formation of microdomains of a ZrTiO₄-like structure. The addition of titanium is effective in increasing the electronic conductivity under reducing conditions. Conductivity as a function of Po₂ and IB results cannot be related to the formation of small polarons during the reduction process. Furthermore, according to the calculations based on the small polaron theory, inconsistent values for the radius of a small polaron (r_p) are obtained in both 10TiYSZ and 10TiTZP. However, large polarons can explain the transport properties in these materials under reducing conditions in agreement with the experimental data.     

Sr2NiMoO6−δ as anode material for LaGaO3-based solid oxide fuel cell

The double-perovskite Sr₂NiMoO_6−δ (SNMO) was investigated as an anode material of a solid oxide fuel cell (SOFC). With a 300 μm thick La_0.9Sr_0.1Ga_0.8Mg_0.2O_3−σ (LSGM) disk as electrolyte and Ba_0.5Sr_0.5Co_0.8Fe_0.2O_3−δ as the cathode, the SNMO anode showed power densities of 819 mW cm⁻² in hydrogen at 1123 K. Moreover, there was no buffer layer between anode and electrolyte, which would reduce design techniques and save design cost. After test no chemical reaction was discovered between anode and electrolyte. The anode exhibited good conductivity and the value was around 60 S cm⁻¹ in H₂. Also it had almost linear thermal expansion from room temperature to 1253 K and the average thermal expansion coefficient was about 12.14 × 10⁻⁶ K⁻¹, which was quite close to that of La_0.9Sr_0.lGa_0.8Mg_0.2O₃ (12.17 × 10⁻⁶ K⁻¹) electrolyte.     

Development of novel LSM/GDC composite and electrochemical characterization of LSM/GDC based cathode-supported direct carbon fuel cells

(La_0.8Sr_0.2)_0.95MnO_3?δ (LSM)–Gd_0.1Ce_0.9O_2?δ (gadolinium-doped ceria, GDC) composite cathode material was developed and characterized in terms of chemical stability, sintering behaviour, electrical conductivity, mechanical strength and microstructures to assess its feasibility as cathode support applications in cathode-supported fuel cell configurations. The sintering inhibition effect of LSM, in the presence of GDC, was observed and clearly demonstrated. The mechanical characterization of developed composites revealed that fracture behaviour is directly affected by pore size distribution. The Weibull strength distribution showed that for bimodal pore size distribution, two different fracture rates were present. Furthermore, the contiguity of LSM and GDC grains was calculated with image analysis, and correlation of microstructural features with mechanical and electrical properties was established. Subsequently, an LSM/GDC-based cathode-supported direct carbon fuel cell (DCFC) with Ni/ScSZ (scandia-stabilised zirconia) anode was successfully fabricated via slurry coating and co-firing techniques. The microstructures of electrodes and electrolyte layers were observed to confirm the desired morphology after co-sintering, and a single cell was electrochemically characterized in solid oxide fuel cell (SOFC) and DCFC mode with ambient air as oxidant. The higher values of open-circuit voltage indicated that the electrolyte layer prepared by vacuum slurry coating is dense enough. The corresponding peak power densities at 850 °C were 450 and 225 mW cm^?2 in SOFC and DCFC mode, respectively. Electrochemical impedance spectroscopy was carried out to observe electrode polarization and ohmic resistance.