高性能Sm0.5Sr0.5CoO3阴极的制备与表征

用固相合成法合成了Sm0.5Sr0.5CoO3 (SSC)中温固体氧化物燃料电池阴极材料.以La0.9Sr0.1Ga0.8Mg0.2O3为电解质,利用多种技术考察了不同温度(1173～1373 K)焙烧的SSC阴极,以及1173 K 焙烧、掺杂La0.8Sr0.2Ga0.8Mg0.15Co0.05O3(LSGMC5)或La0.8Sr0.2Ga0.8Mg0.09Co0.11O3 (LSGMC11)高氧离子电导材料的复合SSC阴极.SEM的结果显示,随着电极焙烧温度的增加,电极的颗粒度增大,孔隙度减小；LSGMC5、LSGMC11的掺杂对电极微观结构影响不大.交流阻抗和极化实验的结果表明,SSC电极的活性随电极焙烧温度的增加而减小,电极的最佳焙烧温度在1173 K左右；掺杂了LSGMC5或LSGMC11的复合SSC电极的活性以及稳定性显著高于SSC电极.     

Sm0.5Sr0.5Co0.4M0.6O3 (M=Co,Mn, Fe)作为IT-SOFCs阴极的结构与性能

通过X射线衍射(XRD)、热重、热膨胀、电导率以及交流阻抗等测试方法, 研究了Sm0.5Sr0.5Co0.4M0.6O3(M=Co, Mn, Fe; 分别简写为SSCC, SSCM, SSCF)作为中低温固体氧化物燃料电池(IT-SOFCs)阴极的结构与性能. 研究表明, 固相法合成的Sm0.5Sr0.5Co0.4M0.6O3均为正交钙钛矿型结构, 材料的结构参数和性能都与M元素半径及M—O的键能有关. 晶胞参数随着Co、Mn、Fe的顺序增大.材料的氧空位浓度、热膨胀系数、电导率、电极催化活性随着Co、Fe、Mn的顺序降低. 同时由于SSCM较低的氧空位浓度, 使得电极反应受到氧在电极内的扩散过程控制, 具有较差的电极催化性能, 而SSCC和SSCF较高的氧空位浓度, 电极反应同时受到电极表面氧还原反应和氧离子在电极中的扩散过程混合控制. 由于SSCF具有较高的氧扩散系数, 使得700 ℃以上SSCF电极表面氧还原电阻(ASR)也低于SSCC的, 因而出现了SSCF的总电极催化活性高于SSCC的现象.     

用湿化学法制备Sm0.5Sr0.5CoO3-La0.8Sr0.2Ga0.8Mg0.15Co0.05O3复合阴极及其性能表征

用湿化学法制备了Sm0.5Sr0.5CoO3(SSC)－La0.8Sr0.2Ga0.8Mg0.15Co0.05O3(LSGMC5)中温固体氧化物燃料电池复合阴极材料，其中SSC用甘氨酸－硝酸盐法合成，LSGMC5用柠檬酸盐法合成。XRD结果表明，甘氨酸－硝酸盐法制备的SSC在焙烧温度大于1223K即表现为单一的钙钛矿结构。随焙烧温度的升高，SSC粉末颗粒增大,导致含有高温烧结SSC的电极与电解质界面结合变差。采用多种技术考察了利用不同温度（1173－1373K）预烧的SSC粉末制备的SSC-LSGMC5阴极上进行的氧还原反应。结果表明，SSC-LSGMC5复合电极的性能显著依赖于电极中SSC粉末的预烧温度，当SSC粉末焙烧温度在1223K附近时，具有最小的欧姆电阻以及氧还原反应极化电阻，1A· cm-2电流密度下的极化过电位为0.077 V。     

高温固体氧化物电解池钙钛矿型氧电极材料Ba_xSr_(1-x)Co_(0.8)Fe_(0.2)O_(3-δ)结构计算与性能研究

研究和开发高性能的钙钛矿型混合电导氧化物是目前高温固体氧化物电解池(SOEC)氧电极材料研究的热点.选择BaxSr1-xCo0.8Fe0.2O3-δ系列材料,通过对材料的容差因子、关口半径、晶格自由体积等计算,以及对平均键能、B位离子的变价能力、催化活性等方面的分析,确定了A位最佳配比.对优化出的Ba0.5Sr0.5Co0.8Fe0.2O3-δ材料的电化学性能进行了研究,并与自制的La0.2Sr0.8MnO3(LSM)氧电极材料进行了比较.结果表明:850℃下阳极极化阻抗(ASR)仅为0.07Ωcm2,远低于LSM;将其应用于SOEC氧电极进行高温电解制氢试验,产氢速率为相同条件下LSM的2.3倍,说明将Ba0.5Sr0.5Co0.8Fe0.2O3-δ用作SOEC阳极材料具有很好的应用前景.     

Sm（0.5）Sr（0.5）Co（0.4）M（0.6）O3（M=Co,Mn,Fe）作为IT-SOFCs阴极的结构与性能

通过X射线衍射(XRD)、热重、热膨胀、电导率以及交流阻抗等测试方法,研究了Sm0.5Sr0.5Co0.4M0.6O3(M=Co,Mn,Fe;分别简写为SSCC,SSCM,SSCF)作为中低温固体氧化物燃料电池(IT-SOFCs)阴极的结构与性能.研究表明,同相法合成的Sm0.5Sr0.5Co0.4M0.6O3均为正交钙钛矿型结构,材料的结构参数和性能都与M元素半径及M-O的键能有关.晶胞参数随着Co、Mn、Fe的顺序增大.材料的氧空位浓度、热膨胀系数、电导率、电极催化活性随着Co、Fe、Mn的顺序降低.同时由于SSCM较低的氧空位浓度,使得电极反应受到氧在电极内的扩散过程控制,具有较差的电极催化性能,而SSCC和SSCF较高的氧空位浓度,电极反应同时受到电极表面氧还原反应和氧离子在电极中的扩散过程混合控制.由于SSCF具有较高的氧扩散系数,使得700 ℃以上SSCF电极表面氧还原电阻(ASR)也低于SSCC的,因而出现了SSCF的总电极催化活性高于SSCC的现象.     

Sm0.5Sr0.5Co1-xCuxO3-δ阴极材料的合成与性能研究

采用尿素-硝酸盐法制备了Sm0.5Sr0.5Co1-xCuxO3-δ(x=0～0.5)阴极材料.用TG-DSC,SEM,XRD和热膨胀仪对材料的形成过程、晶体结构、烧结体的微观结构及热膨胀性能进行了表征.用直流四端子法测试材料在500～800℃范围内的电导率.结果表明,制备样品的主晶相为正交钙钛矿结构,体系含有杂相;电导率随温度和Cu含量的变化关系表现为,x≤0.2时的样品随温度升高电导率降低,x≥0.3时随温度升高电导率增大,组成为x=0.2的样品电导率最高,500℃达到703.1 S·cm-1.材料的热膨胀系数随掺杂的Cu含量增加而降低.     

Ba0.5Sr0.5Co0.8Fe0.2O3-δ为阴极的中温固体氧化物燃料电池

 通过在阴极与氧化钇稳定的氧化锆电解质间添加Gd0.1Ce0.9O1.95 (GDC)隔层,成功地将Ba0.5Sr0.5Co0.8Fe0.2O3-δ (BSCF)阴极应用在中温固体氧化物燃料电池上. 由BSCF膜的高透氧率可知,BSCF在中温范围内具有很高的氧离子电导率. 在添加GDC隔层后,电池以空气为氧化剂时显示了很高的性能,极化电阻急剧下降,表明GDC隔层的添加是必要和有效的.     

Sm0.5Sr0.5CoO3阴极氧还原动力学

利用极化、交流阻抗技术考察了担载于La0.9Sr0.1Ga0.8Mg0.2O3(LSGM)电解质上的Sm0.5Sr0.5CoO3- La0.8Sr0.2Ga0.8Mg0.15Co0.05O3(SSC-LSGMC5)复合阴极的氧还原反应动力学.在SSC-LSGMC5阴极氧还原反应的阻抗谱中可以观察到明显的两个半圆.高频环的电导与氧分压无关,低频环的电导正比于氧分压的0.5次方.并且低频环的氧分压级数随着反应温度的降低而减小,可能对应于吸附氧原子的扩散过程. SSC-LSGMC5极化曲线与经典的Butler-Volmer方程吻合.阴、阳极的电荷转移系数均为1左右,交换电流密度的氧分压级数为1/4,对应于电荷转移过程. 实验结果显示SSC-LSGMC5上的氧还原反应机制随反应条件的不同而发生变化.     

La0.9M0.1Ga0.8Mg0.2O3-α的中温质子导电性及其在常压合成氨中的应用

采用水热沉淀法制备了La0.9M0.1Ga0.8 Mg0.2O3-a(M=Ca2+,Sr2+,Ba2+)陶瓷样品的前驱体,沉淀剂来自尿素在水热条件下的水解产物.前驱体经煅烧和烧结后得到陶瓷样品.XRD显示样品具有单一的斜方晶LaGaO3钙钛矿结构.同位素效应和氢的电化学透过(氢泵)实验证明陶瓷样品具有质子导电性.用AC阻抗谱法测定了样品在300~600℃、氢气气氛中的质子电导率,其人小取决于La位掺杂的碱土金属离子:σ(M=Sr2+)>σ(M=Ba2+)>σ(M=Ca2+).以La0.9M0.1Ga0.8Mg0.2O3-a为固体电解质进行了常压合成氨,最佳合成温度为520℃.当施加的电流密度为1mA-cm-2、合成温度为520℃时,氨产率分别为:1.63X 10-9 mol·s-1cm-2(M=Ca2+),2.53X 10-9 mol·s-1·cm-2(M=Sr2+)和2.04X10-9mol·s-1,cm-2(M=Ba2+).     

固-溶法制备中温固体氧化物燃料电池高性能La_(0.8)Sr_(0.2)MnO_3-Ba_(0.5)Sr_(0.5)Co_(0.8)Fe_(0.2)O_3阴极（英文）

研究了新型固溶法合成La0.8Sr0.2MnO3(LSM)包覆Ba0.5Sr0.5Co0.8Fe0.2O3(BSCF)复合粉体(LSM-BSCF),并探讨了其作为中温固体氧化物燃料电池阴极材料的电化学性能.LSM-BSCF阴极结合了LSM和BSCF阴极的优点,不仅增大了三相界面,而且稳定了微观结构.当温度为600儃750°C时,其极化阻抗为0.61儃0.09Ω·cm2.与溶液注入法制备的高性能电极相比,极大地提高了性能稳定性.     

Phase stability in the systems AeAl(2-x)Mgx (Ae = Ca, Sr, Ba): electron concentration and size controlled variations on the laves phase structural theme

The systems AeAl(2-x)Mgx (Ae = Ca, Sr, Ba) display electron concentration induced Laves phase structural changes. However, the complete sequence MgCu2 --> MgNi2 --> MgZn2 with increasing x (decreasing electron count) is only observed for Ae = Ca. Compounds SrAl(2-x)Mgx (0 < x < or = 2) and BaAl(2-x)Mgx (x = 0.85 and 2.0) were synthesized and structurally characterized by X-ray diffraction experiments. For the Sr system the structural sequence CeCu2 --> MgNi2 --> MgZn2 occurs with increasing Mg content x. Thus, larger Sr does not allow the realization of the MgCu2 structure at low x. For Ae = Ba a binary compound BaAl2 does not exist, but more Ba-rich Ba7Al13 forms. The reinvestigation of the crystal structure of Ba7Al13 by selected area and convergent beam electron diffraction in a transmission electron microscope revealed a superstructure, which subsequently could be refined from single X-ray diffraction data. The formula unit of the superstructure is Ba21Al40 (space group P31m, Z = 1, a = 10.568(1) angstroms, c = 17.205(6) angstroms). In Ba21Al40 a size match problem between Ba and Al present in Ba7Al13 is resolved. The structure of Ba7Al13 (Ba21Al40) can be considered as a Ba excess variant of the hexagonal MgNi2 Laves phase type structure. An incommensurately modulated variant of the MgNi2 structure is obtained for phases BaAl(2-x)Mgx with x = 0.8-1. At even higher Mg concentrations a structural change to the proper MgZn2 type structure takes place.     

Influence of disorder-to-order transition on lattice thermal expansion and oxide ion conductivity in (Ca(x)Gd(1-x))(2)(Zr(1-x)M(x))2O7 pyrochlore solid solutions

The effect of simultaneous substitutions of Ca at A site and Nb or Ta at B site in pyrochlore-type solid solutions: (Ca(x)Gd(1-x))(2)(Zr(1-x)M(x))(2)O(7) (x = 0.1, 0.2, 0.3, 0.4, 0.5 and M = Nb or Ta) were studied by powder X-ray diffraction (XRD), FT NIR Raman spectroscopic techniques and transmission electron microscopy. The solid solutions were prepared by the conventional high-temperature ceramic route. The XRD results and Rietveld analysis revealed that the defect fluorite structure of Gd(2)Zr(2)O(7) progressively changed to a more ordered pyrochlore phase by simultaneous substitutions at A and B sites. Raman spectroscopy reveals the progressive ordering in the anion sublattice with simultaneous doping. High-resolution images and selected-area electron diffraction patterns obtained from TEM confirms the XRD and Raman spectroscopic results. High-temperature XRD studies show that the lattice expansion coefficient in these pyrochlore oxides is of the order of 10(-6) K(-1). Lattice thermal expansion coefficient increases with increase of disorder in pyrochlore oxides, and hence the variation of thermal expansion coefficient with composition is also a good indicator of disordering in pyrochlore-type oxides. The ionic conducting properties of the samples were characterised by impedance spectroscopy, and it was found that Nb-doped compositions show a considerable change in conductivity near the phase boundary of disordered pyrochlore and defect fluorite phases.     

Ca(2+)/vacancies and O2-/F- ordering in new oxyfluoride pyrochlores Li(2x)Ca1.5-x square 0.5-xM2O6F (M = Nb,Ta) for 0 < or = x < or = 0.5

New oxyfluorides Li(2x)Ca(1.5-x) square (0.5-x)M2O6F (M = Nb, Ta), belonging to the cubic pyrochlore structural type (Z = 8, a approximately 10.5 angstroms), were synthesized by solid state reaction for 0 < or = x < or = 0.5. XRD data allowed us to determine their structures from single crystals for the two alpha and beta-Ca(1.5) square (0.5)Nb2O6F forms and from powder samples for the others. This characterisation was completed by TEM and solid state 19F NMR experiments. For the Ca(1.5) square (0.5)M2O6F (x = 0) pyrochlore phases, the presence of a double ordering phenomenon is demonstrated, involving on one hand the Ca(2+) ions and the vacancies and on the other hand the oxide and the fluoride anions which are strictly located in the 8b sites of the Fd3m aristotype space group. The Ca(2+) ions/vacancies ordering leads to a reversible phase transition, a (P4(3)32) <--> beta (Fd3m). The 19F NMR study strongly suggests that, in the beta-phases, the fluoride ions are only on average at the centre of the Ca3 square tetrahedron. It shows that slightly different Ca-F distances occuring in alpha-Ca(1.5) square (0.5)Nb2O6F may be related to a more difficult thermal ionic and vacancies diffusion process than in the tantalate compound. This may explain the hysteresis phenomenon presented by the phase transition. A solid solution Li(2x)Ca(1.5-x) square (0.5-x) Ta2O6F (0 < or = x < or = 0.5) was prepared and the order-disorder phase transition observed for Ca(1.5) square (0.5)M2MO6F compounds disappears for all the other compositions where less or no more vacancies exist in the 16d sites. In the LiCaM2O6F compounds, the 19F NMR study allows us to determine the Ca(2+) and Li+ ions distributions around the fluoride ions and shows that the [FLi2Ca2] environment is clearly favoured.     

Synthesis and characterisation of alkaline earth bis(diphenylphosphano)metallocene complexes and heterobimetallic alkaline earth metal/platinum(II) complexes [Ae(thf)(x)(η5-C5H4PPh2)2Pt(Me)2] (Ae = Ca, Sr, Ba)

A series of alkaline earth metallocene complexes carrying the diphenylphosphanocyclopentadienyl ligand, [Ae(L)(x)(η(5)-C(5)H(4)PPh(2))(2)] (Ae = Ca, L = thf, x = 1 (6a); Ae = Ca, L = dme, x = 1 (6b); Ae = Sr, L = thf, x = 1 (7); Ae = Ba, L = thf, x = 1 (8a); Ae = Ba, L = dme, x = 2 (8b)), were prepared by redox transmetallation/protolysis from the free metals, diphenylmercury and diphenylphosphanocyclopentadiene. These complexes were characterised using multinuclear NMR spectroscopy and two by single crystal X-ray diffraction. [Ca(dme)(η(5)-C(5)H(4)PPh(2))(2)] (6b) is a discrete neutral monomeric eight coordinate molecule in which the phosphorus atoms are not coordinated to the calcium ion and the larger barium analogue, ten-coordinate [Ba(dme)(2)(η(5)-C(5)H(4)PPh(2))(2)] (8b), has an extremely bent sandwich structure due to the two dme ligands attached to the metal. Bimetallic complexes, [Ae(thf)(x)(η(5)-C(5)H(4)PPh(2))(2)Pt(Me)(2)].(solv) (Ae = Ca, L = thf, x = 2, solv = 1.5thf (9); Ae = Sr, L = thf, x = 3, solv = 1.5thf (10); Ae = Ba, L = thf, x = 3, solv = thf (11)) were obtained by reaction of the homometallic complexes with [Pt(cod)(Me)(2)]. The crystal structures of [Ca(thf)(2)(η(5)-C(5)H(4)PPh(2))(2)Pt(Me)(2)].1.5thf (9), [Sr(thf)(3)(η(5)-C(5)H(4)PPh(2))(2)Pt(Me)(2)].1.5thf (10) and [Ba(thf)(3)(η(5)-C(5)H(4)PPh(2))(2)Pt(Me)(2)].thf (11) show the eight (calcium) and nine coordinate (strontium and barium) fragments acting as a chelating metalloligand attached to the square planar platinum through the phosphorus donor atoms. The solution chemistry of these bimetallic complexes has been investigated by NMR spectroscopy, electro-spray ionisation mass spectrometry and conductivity experiments which indicate that the bimetallic compounds persist in solution.     

Crystal structure and carbon vacancy hardening of (W0.5Al0.5)C1-x prepared by a solid-state reaction.

Novel solid solutions of aluminum in tungsten carbide (WC) with or without carbon vacancies, which can be expressed by the chemical formula (W(0.5)Al(0.5))C(1-x) (x=0.0-0.5), have been synthesized by the solid-state reaction of W(0.5)Al(0.5) alloy and the proper amount of carbon at around 1673 K in vacuum. The reaction time decreases from 73 to 50 h on increasing the carbon vacancy concentration from 0 to 50 %. The formation of the intended products is certified, by X-ray diffraction, environmental scanning electron microscopy-energy-dispersive X-ray analysis, and inductively coupled plasma-atomic emission spectroscopy, even though the carbon vacancy concentration reaches the astonishing value of 50 %. The as-prepared (W(0.5)Al(0.5))C(1-x) samples have been identified as the hexagonal WC-type structure belonging to the space group P6m2 (Z=1). Moreover, the crystallographic results reveal that the substituting aluminum atoms in the WC are located in the 1a site (the W atom position of the WC structure) and the cell parameters decrease slightly with increasing vacancy concentration. The hardness of the (W(0.5)Al(0.5))C(1-x) system increases up to a maximum 2659 kg mm(-2) at a carbon vacancy concentration of about 35 %, and the density of (W(0.5)Al(0.5))C(1-x) is far lower than that of WC.     

Enhanced high-temperature thermoelectric performance of Yb(14-x)Ca(x)MnSb11

The high temperature p-type thermoelectric material Yb(14)MnSb(11) has been of increasing research interest since its high temperature thermoelectric properties were first measured in 2006. Subsequent substitutions of Zn, Al, and La into the structure have shown that this material can be further optimized by altering the carrier concentration or by reduction of spin-disorder scattering. Here the properties of the Yb(14-x)Ca(x)MnSb(11) solid solution series where isovalent Ca(2+) is substituted for Yb(2+) will be presented. Crystals of the Yb(14-x)Ca(x)MnSb(11) solid solution series were made by Sn-flux (x = 2, 4, 6, 8) with the following ratio of elements: (14-x)Yb: xCa: 6 Mn: 11Sb: 86Sn, and their structures determined by single crystal X-ray diffraction. The density of the material significantly decreases by over 2 g/cm(3) as more Ca is added (from x = 1 to 8), because of the lighter mass of Ca. The resulting lower density is beneficial from a device manufacturing perspective where there is often a trade-off with the specific power per kilogram. The compounds crystallize in the Ca(14)AlSb(11) structure type. The Ca substitution contributes to systematic lengthening the Mn-Sb bond while shortening the Sb-Sb bond in the 3 atom linear unit with increasing amounts of Ca. Temperature dependent thermoelectric properties, Seebeck, electrical resistivity, and thermal conductivity were measured from room temperature to 1273 K. Substitution of Yb with Ca improves the Seebeck coefficient while decreasing the thermal conductivity, along with decreasing the carrier concentration in this p-type material resulting in an enhanced thermoelectric figure of merit, zT, compared to Yb(14)MnSb(11).     

Mn(I) in an extended oxide: the synthesis and characterization of La(1-x)Ca(x)MnO(2+δ) (0.6 ≤ x ≤ 1)

Reduction of La(1-x)Ca(x)MnO(3) (0.6 ≤ x ≤ 1) perovskite phases with sodium hydride yields materials of composition La(1-x)Ca(x)MnO(2+δ). The calcium-rich phases (x = 0.9, 1) adopt (La(0.9)Ca(0.1))(0.5)Mn(0.5)O disordered rocksalt structures. However local structure analysis using reverse Monte Carlo refinement of models against pair distribution functions obtained from neutron total scattering data reveals lanthanum-rich La(1-x)Ca(x)MnO(2+δ) (x = 0.6, 0.67, 0.7) phases adopt disordered structures consisting of an intergrowth of sheets of MnO(6) octahedra and sheets of MnO(4) tetrahedra. X-ray absorption data confirm the presence of Mn(I) centers in La(1-x)Ca(x)MnO(2+δ) phases with x < 1. Low-temperature neutron diffraction data reveal La(1-x)Ca(x)MnO(2+δ) (x = 0.6, 0.67, 0.7) phases become antiferromagnetically ordered at low temperature.     

A molecular dynamics study of the atomic structure of (CaO)x(SiO2)1-x glasses

The local atomic environment of Ca in (CaO)x(SiO2)1-x glasses is of interest because of the role of Ca in soda-lime glass, the application of calcium silicate glasses as biomaterials, and the previous experimental measurement of the Ca-Ca correlation in CaSiO(3) glass. Molecular dynamics has been used to obtain models of (CaO)x(SiO2)1-x glasses with x = 0, 0.1, 0.2, 0.3, 0.4, and 0.5, and with approximately 1000 atoms and size approximately 25 A. As expected, the models contain a tetrahedral silica network, the connectivity of which decreases as x increases. In the glass-forming region, i.e., x = 0.4 and 0.5, Ca has a mixture of 6- and 7-fold coordination. Bridging oxygen makes an important contribution to the coordination of Ca, with most bridging oxygens coordinated to 2 Si plus 1 Ca. The x = 0.5 model is in reasonable agreement with previous experimental studies, and does not substantiate the previous theory of cation ordering, which predicted Ca arranged in sheets. In the phase-separated region, i.e., x = 0.1 and 0.2, there is marked clustering of Ca.     

Ce1-xNixO2/Al2O3/FeCrAl催化剂的制备及其甲烷催化燃烧性能

以FeCrA l合金薄片为基体,A l2O3为过渡载体,Ce1-xN ixO2(x=0.1-0.3)、CeO2和N iO为活性组分,制备了Ce1-xN ixO2/A l2O3/FeCrA l、CeO2/A l2O3/FeCrA l和N iO/A l2O3/FeCrA l金属基整体式催化剂,在固定床微型反应器中评价了催化剂的甲烷催化燃烧性能,用SEM、XRD、TPR等方法对催化剂的物相、表面形貌和氧化还原性进行了表征.结果表明,Ce1-xN ixO2在催化剂表面的分散性比CeO2和N iO要好;Ce1-xN ixO2/A l2O3/FeCrA l(x=0.1-0.3)催化剂具有好的催化活性和高温稳定性,CeO2/A l2O3/FeCrA l和N iO/A l2O3/FeCrA l催化剂有好的初活性但高温稳定性较差;活性组分与A l2O3和FeCrA l金属基体之间存在较强的相互作用.     

磁铅石型复合氧化物LaNi_xCo_(1-x)Al_(11)O_(19+δ)催化剂上CH_4和CO_2重整反应的研究

考察了磁铅石型复合氧化物LaNi_(0.5)M_(0.5)Al_(11)O_(19 + δ) (M = Co, Fe, Mn, Cu)和LaNi_xCo_(1-x)Al_(11)O_(19+δ)催化剂在CH_4与CO_2重整制合成 气反应中的催化活性，并应用XRD，TPR，UV-DRS技术着重表征LaNi_xCo_(1-x)Al_ (11)O_(19+δ)催化剂的结构和性能。研究结果表明该系列催化剂具有相同的晶体 结构和相似的还原稳定性。对不同过渡金属取代的催化剂来说，以LaNi_(0.5)Co_ (0.5)Al_(11)O_(19+δ)催化剂具有最好的反应活性。而对于LaNi_xCo_(1-x)Al_ (11)O_(19+δ)系列催化剂，当x ≤ 0.375时，随x值的增大，催化活性明显提高， 但在0.375 ≤ x ≤ 1.0范围内，催化活性几乎保持不变。由此得到结论，对于此 反应来说，控制Ni量在0.375 ≤ x ≤ 0.50范围内比较合适。