燃料電池可直接將燃料因氧化產生的化學能轉變成電能的一種電化學元件，在一個典型的固態氧化物燃料電池 (SOFCs) 中，釔安定化氧化鋯 (YSZ) 為常用的電解質材料，其導電率在800℃時為0.02 Scm-1。鈣鈦礦結構之LaGaO3在適當的摻雜各種異價離子後，在高溫下具有非常低之電阻率且幾乎為一完全的氧離子導體，因此有潛力取代YSZ成為較佳之固態氧化物燃料電池的固態電解質材料。同樣是稀土族鈣鈦礦結構的LaAlO3也可藉由低價數陽離子的取代而提升其離子導電率，其優點為成本遠低於LaGaO3。因此如何製備高導電性之鑭系固態電解質，並且將其薄膜化為電池組，為本研究之重點。
本研究首先探討二價的鍶、鎂離子在不同的添加量對LaAlO3及LaGaO3晶體結構及導電率的影響。第二部分在探討在利用水熱反應法合成奈米La0.8Sr0.2Ga0.8Mg0.2O2.8粉體，藉由良的好分散性及可降低燒結溫度等特性，並利用電泳沉積法製備Pt/ La0.8Sr0.2Ga0.8Mg0.2O2.8/LSM陰極支撐型單電池，量測其發電效率。第三部分在探討利用低成本的LaAlO3電解質藉由Ba與Y離子的添加，合成高導電性的La0.9Ba0.1Al0.9Y0.1O2.9電解質，最後利用電泳沉積法及網印技術組裝為NiO-YSZ/SDC/La0.9Ba0.1Al0.9Y0.1O2.9/LSM陰極支撐型單電池，並測試其發電效率。
添加鍶與鎂之LaGaO3與LaAlO3固態電解質其固溶行為有很大的不同，而不同的添加劑對於LaGaO3與LaAlO3鈣鈦礦氧離子導體的導電性也有很大的影響。在LaAlO3系統中，Mg離子之溶解度小於10 mol.%，是因為Mg與Al之離子半徑差異太大；而對於Sr離子的溶解量則高達20 mol.%。在同時添加Mg與Sr離子時，Sr離子的存在會促進Mg離子固溶度的增加。而在LaGaO3系統中，Mg離子之固溶量可達20 mol.%，但卻只有不到10 mol.%之Sr離子可以固溶於LaGaO3中。而在同時添加Mg與Sr離子時，Mg離子的存在可以提昇Sr離子的溶解度，這是由於Mg離子的存在可以將晶格撐大，因而促進Sr離子的固溶。在添加劑的固溶極限內，LaGaO3與LaAlO3的導電率都會因為添加劑含量的增加而提昇。超過了溶解極限，則會因為第二相的生成而使材料之導電率急遽下降。
利用含有尿素為沉澱劑之水熱法於200 ℃下合成La0.8Sr0.2Ga0.8Mg0.2O2.8 奈米粉體。由X光繞射分析可知，在900 ℃下煆燒12小時即可得到La0.8Sr0.2Ga0.8Mg0.2O2.8相。而在1100℃下煆燒即有粉體頸縮 (necking) 之現象，表示La0.8Sr0.2Ga0.8Mg0.2O2.8粉體有開始燒結之現象。在1400 ℃燒結3小時，可得相對密度98 %之緻密塊材，此La0.8Sr0.2Ga0.8Mg0.2O2.8塊材在800 ℃之導電率為5.6x10-2 Scm-1。利用電泳沉積法將La0.8Sr0.2Ga0.8Mg0.2O2.8薄膜沉積在La0.8Sr0.2MnO3基材上，於1400 ℃下共燒3小時，可得65 μm之緻密La0.8Sr0.2Ga0.8Mg0.2O2.8薄膜。將燒結好之圓形試片，塗以白金為陽極，於800 ℃下測試單電池之性能，可得0.97 V之開路電壓與最大0.68 W/cm2之電力密度。顯示電泳沉積法可以製備出良好之電解質薄膜。
在Ba與Y離子添加之LaAlO3系統中，Ba離子之固溶量只有5 mol.%，而Y離子之固溶量有10 mol.%。而Ba與Y離子同時添加時，因為大離子半徑之Y的存在，可以促進Ba離子在LaAlO3系統中的固溶量，因此可以同時固溶10 mol.%Ba與10 mol.% Y離子。La0.97Ba0.03AlO2.985 與LaAl0.9Y0.1O2.95在800 ℃導電率可高達2.68x10-4 Scm-1與1.26x10-3 Scm-1，而含雙添劑加之La0.9Ba0.1Al0.9Y0.1O2.9 (LBAYO) 則為1.84x10-2 Scm-1。利用電泳沉積法可製備出陰極支撐之NiO-YSZ/SDC/LBAYO/La0.8Sr0.2MnO3單電池，LBAYO電解質之厚度為63 μm，為一均勻平整之電解質層，於800 ℃工作溫度下操作，其最大電力密度為0.306 W/cm2。

Fuel cells are able to convert the chemical energy of fuel directly into electrical energy. A typical solid oxide fuel cells (SOFCs) operates near 800 ℃ and yttria-stabilized zirconia (YSZ) is the most widely used electrolyte, which exhibits an oxide ion conductivity of about 0.02 Scm-1. Doped lanthanum gallate of the perovskite structure type has been investigated as the replacement for YSZ due to its low resistivity and almost completely ionic conductor. It was also found that lanthanum aluminate of the perovskite structure type exhibit considerable ionic conduction by the addition of lower-valent cations. The advantage of this material is more inexpensive element, such as Al. From the point of view of lanthanum solid state electrolyte materials, high conductivity and thin film process ability, must be considerable.
In the beginning of this study, various amounts of Sr ions and Mg ions were added into LaAlO3 and LaGaO3 by repeated calcination and mixing. Undoped and doped LaAlO3 and LaGaO3 were characterized by XRD, which were used for the structural analysis. The DC method technique was used to determine the electrical conductivity of sintered samples at various temperatures. In the secondly, a hydrothermal precipitation method was used to synthesize nanosized La0.8Sr0.2Ga0.8Mg0.2O2.8 solid solutions with good structural homogeneity and reduced sintering temperature. The microstructure and electrical properties of this system were also investigated. Finally, the electrophoretic behavior of the La0.8Sr0.2Ga0.8Mg0.2O2.8 thin films under different deposition conditions was characterized. The cell performance of the cathode supported La0.8Sr0.2Ga0.8Mg0.2O2.8 thin films was investigated in the temperature range of 600 to 800 ℃. The third part, the conductivity of cost-effective LaAlO3 was enhanced by doping Ba and Y ions into A- and B-site of perovskite structure. The electrolyte La0.9Ba0.1Al0.9Y0.1O2.9 film was fabricated on the porous La0.8Sr0.2MnO3 substrate using an electrophoretic deposition (EPD) process to assemble a high-performance SOFC. The cell performance of the cathode-supported La0.9Ba0.1Al0.9Y0.1O2.9 cells was investigated at the temperature range from 600 to 800 ℃.
In the LaAlO3 system, the solubility of Mg ion was less than 10 mol.% due to the mismatch of ionic radius between the Mg and Al cations. The substitution of Sr ion in the La-cation sublattice was as high as 20 mol.%. With the doubly-doping of Sr ion and Mg ion in LaAlO3, the enhancement of Mg ion solubility was also observed. However, further addition of Mg ion tends to lower the solubility of Sr ion from 20 to 10 mol.%. This result can be rationalized by the reduced distance between Mg ion and Sr ion that caused the cation–cation repulsion in the perovskite structure. In the singly-doped LaGaO3 systems, the solubility of Mg ion was found to be 20 mol.%. However, only less than 10 mol.% of the La-cation sublattice could be substituted by Sr ions. With the doubly-doping of Sr ion and Mg ion, the solubility of Sr ion was significantly enhanced by the addition of Mg ion. It is believed that the solubility enhancement of Sr ions is due to the expanded lattice caused by the addition of Mg ion. Within the solubility limit of the aliovalent cations, the ionic conductivities of both LaAlO3 and LaGaO3 systems increased with the increasing concentration of foreign cations. After the solubility limits in both doped LaAlO3 and LaGaO3 were reached, the segregation of the second phase tends to lower the ionic conductivity drastically.
Solid electrolyte powder having a composition of La0.8Sr0.2Ga0.8Mg0.2O2.8 was prepared by the decomposition of a urea-containing solution under hydrothermal conditions and followed by calcination in air. X-ray diffraction patterns indicate a single perovskite phase formed without traceable impurities after calcination at 900 ℃ for 12 hours. The La0.8Sr0.2Ga0.8Mg0.2O2.8 powder agglomerated together due to the necking and bonding behavior at 1100 ℃. This result also indicates that La0.8Sr0.2Ga0.8Mg0.2O2.8 powder may be densified at lower temperature when the powder is synthesized using a hydrothermal process. The hydrothermally processed La0.8Sr0.2Ga0.8Mg0.2O2.8 samples was sintered at 1400 ℃ for 3h. The relative density of La0.8Sr0.2Ga0.8Mg0.2O2.8 bulk sample was up to 98 %. The electrical conductivity is 5.6x10-2 Scm-1 at the temperature of 800 ℃. A La0.8Sr0.2Ga0.8Mg0.2O2.8 thin film on a La0.8Sr0.2MnO3 porous cathode substrate was prepared, using electrophoretic deposition to fabricate a solid oxide fuel cell. Dense La0.8Sr0.2Ga0.8Mg0.2O2.8 films with a thickness of about 65 μm have been successfully fabricated on porous LSM substrates when sintered at 1400 ℃ for 3h. A planar-type SOFC was fabricated, using Pt as the anode and La0.8Sr0.2Ga0.8Mg0.2O2.8 film (65 μm) that had been deposited onto the LSM substrate as the electrolyte and cathode. The cell exhibited an open circuit voltage of 0.97 V and a maximum power density of 0.68 W/cm2. Thus, the EPD method could be used as a colloidal process to prepare La0.8Sr0.2Ga0.8Mg0.2O2.8 thin-film electrolytes for SOFCs.
Cations, Ba2+ and Y3+, were added into the respective cation sublattice of another perovskite, LaAlO3 in this study. The solubility of Ba in the La-cation sublattice was found to be only 5%. In the B-site sublattice, the solubility of Y ion in Al-cation sites was less than 15 %. With double doping of Ba and Y in LaAlO3, the enhancement of Ba solubility to 10 % was also observed. Within the solubility limit of singly doped LaAlO3, the ionic conductivities of doped LaAlO3 were slightly increased with the increasing dopant concentration. For La0.97Ba0.03AlO2.985 and LaAl0.9Y0.1O2.95, the conductivities measured were 2.68x10-4 Scm-1 and 1.26x10-4 Scm-1 at 800℃, respectively. It was rather interesting that the conductivities of the doubly doped La0.9Ba0.1Al0.9Y0.1O2.9 (LBAYO) was enhanced to 1.84x10-2 Scm-1 at 800℃. Cathode-supported cells consisting of an NiO/YSZ anode, a thin LBAYO electrolyte (63 μm), a samarium doped ceria (SDC) interlayer, and a La0.8Sr0.2MnO3 (LSM) cathode were fabricated. The LBAYO electrolyte film was prepared on conductive LSM substrates using the EPD technique. The cathode-supported structure, consisting of an LBAYO film on a porous LSM substrate, was co-fired at 1450 ℃ for 2 h. A crack-free LBAYO film with uniform thickness supported on a porous LSM substrate was obtained. The maximum power density of an NiO-YSZ/SDC/LBAYO/LSM cell with a 63μm thick electrolyte was 0.306 W/cm2 at 800 ℃, using H2 as fuel and air as the oxidant.

1. Ryan O'Hayre, S.W. Cha, W. Colella and F.B. Prinz, Fuel Cell Fundamentals, pp.10-12, J. Wiley, New York, 2006.
2. J. Larminie and A. Dicks, Fuel cell systems explained, 2nd edition, pp14-16, J. Wiley, New York, 2003.
3. N.Q. Minh, “Ceramic fuel cells,” J. Am. Ceram. Soc., 76[3] (1993) 563-588.
4. S.C. Singhal, "Science and technology of solid-oxide fuel cells," Mat. Res. Bull., 25[3] (2000) 16-21.
5. N.Q. Minh, “Solid oxide fuel cell technology - features and applications,” Solid State Ionics, 174 (2004) 271-277.
6. H. Inaba and H. Tagawa, “Ceria-based solid electrolytes,” Solid State Ionics, 83 (1996) 1-16.
7. V.V. Kharton, F.M.B. Marques and A. Atkinson, “Transport properties of solid oxide electrolyte ceramics: a brief review,” Solid State Ionics, 174 (2004) 135-149.
8. S.P.S. Badwal and K. Foger, “Solid oxide electrolyte fuel cell review,” Ceram. Int., 22 (1996) 257-265.
9. H. Yokokawa, N. Sakai, T. Horita, K. Yamaji and M.E. Brito, “Electrolytes for solid-oxide fuel cells,” Mat. Res. Bull., 30 [3] (2005) 591-595.
10. U. Pal and S. C. Singhal, “Electrochemical vapor deposition of yttria-stabilized zirconia films,” J. Electrochem. Soc., 137 (1990) 2937-2941.
11. J.P. Dekker, V.E.J. van Dieten and J. Schoonman “The growth of electrochemical vapor deposited YSZ films,” Solid State Ionics, 51 (1992) 143-145.
12. L.G.J. de Haart, Y.S Lin, K.J de Vries, A.J Burggraaf, “On the kinetic study of electrochemical vapour deposition,” Solid State Ionics, 47 (1991) 331-336.
13. H. Yamane and T. Hirai, “Preparation of ZrO2-film by oxidation of ZrCl4,” J. Mater. Sci. Lett., 6 (1987) 1229.
14. H. Yamane and T. Hirai, “Yttria stabilized Zirconia transparent films prepared by chemical vapor deposition,”J. Cryst. Growth, 94 (1989) 880.
15. C.R. Aita and C.K. Kwok, “Fundamental optical absorption edge of sputter- deposited zirconia and yttria,” J. Am. Ceram. Soc., 73 [11] (1990) 3209-3214.
16. N. Nakagawa, H. Yoshioka, C. Kuroda and M. Ishida, “Electrode performance of a thin-film YSZ cell set on a porous ceramic substrate by rf sputtering technique,” Solid State Ionics, 35 (1989) 249-255.
17. S. Tekeli and U. Demir, “Colloidal processing, sintering and static grain growth behaviour of alumina-doped cubic zirconia,” Ceram. Int., 31[7] (2005) 973-980.
18. D. Rotureau, J.P. Viricelle, C. Pijolat, N. Caillol and M. Pijolat, “Development of a planar SOFC device using screen-printing technology,” J. Eur. Ceram. Soc., 25[12] (2005) 2633-2636.
19. D. W. Dees, T. D. Claar, T. E. Easler, D. C. Fee, and F. C. Mrazek, “Conductivity of Porous Ni/ZrO2-Y2O3 Cermets," J. Electrochem. Soc., 134 (1987) 2141-2146.
20. P. Sarkar and P.S. Nicholson, “Electrophoretic Deposition (EPD): Mechanisms, Kinetics, and Application to Ceramics,” J. Am. Ceram. Soc., 79[8] (1996) 1987-2002.
21. T. Ishihara, K. Sato, Y. Takita, “Electrophoretic Deposition of Y2O3-Stabilized ZrO2 Electrolyte Films in Solid Oxide Fuel Cells,” J. Am. Ceram. Soc., 79[4] (1996) 913-919.
22. T. Ishihara, H. Matsuda and Y. Takits, “Doped LaGaO3 perovskite type oxide as a new oxide ionic conductor,” J. Am. Chem. Soc., 116 (1994) 3801-3803.
23. M. Feng and J.B. Goodenough, “A Superior oxide-ion electrolyte,” Eur. J. Solid State Inorg. Chem., 31 (1994) 663-672.
24. K. Huang, M. Feng, and J.B. Goodenough, “Sol-Gel synthesis of a new oxide-ion conductor Sr- and Mg-doped LaGaO3 perovskite,” J. Am. Ceram. Soc., 79[4] (1996) 1100-1104.
25. P. Huang and A. Petric, “Superior oxygen ion conductivity of lanthanum gallate doped with strontium and magnesium,” J. Electrochem. Soc., 143[5] (1996) 1644-1648.
26. J.W. Stevenson, T.R. Armstrong, D.E. McCready, L.R. Pederson, and W.J. Weber, “Processing and electrical properties of alkaline earth-doped lanthanum gallate,” J. Electrochem. Soc., 144[10] (1997) 3613-3620.
27. K. Huang, R.S. Tichy, J.B. Goodenough, “Superior perovskite oxide-ion conductor; strontium- and magnesium-doped LaGaO3: I, phase relationships and electrical properties,” J. Am. Ceram. Soc., 81[10] (1998) 2565-2575.
28. K. Huang, R.S. Tichy, J.B. Goodenough, “Superior perovskite oxide-ion conductor; strontium- and magnesium-doped LaGaO3: II, ac impedance spectroscopy,” J. Am. Ceram. Soc., 81[10] (1998) 2576-2580.
29. K. Huang, R.S. Tichy, J.B. Goodenough, C. Milliken, “Superior perovskite oxide-ion conductor; strontium- and magnesium-doped LaGaO3: III, performance tests of single ceramic fuel cells,” J. Am. Ceram. Soc., 81[10] (1998) 2581-2585.
30. T.Y. Chen and K.Z. Fung, “Synthesis of and densification of oxygen-conducting La0.8Sr0.2Ga0.8Mg0.2O2.8 nano powder prepared from a low temperature hydrothermal urea precipitation process,”J. Eur. Ceram. Soc., 28 (2008) 803-810.
31. T.Y. Chen and K.Z. Fung, “A and B-site substitution of the solid electrolyte LaGaO3 and LaAlO3 with the alkaline-earth oxides MgO and SrO,” J. Alloy Comp., 368 (2004) 106-115.
32. T.Y. Chen and K.Z. Fung, “Comparison of dissolution behavior and ionic conduction between Sr and/or Mg doped LaGaO3 and LaAlO3,” J. Power Sources, 132 (2004) 1-10.
33. T.Y. Chen and K.Z. Fung, “Effect of divalent dopants on crystal structure and electrical properties of LaAlO3 perovskite,” J. Phy. Chem. Solid, 69 (2008) 540-546.
34. T. Takahashi and H. Iwahara, “Ionic conduction in perovskite-type oxide solid solution and its application to the solid electrolyte fuel cell,” Energy Conversion, 11 (1971) 105-111.
35. J.A. Kilner, P. Barrow, R.J. Brook, and M.J. Norgett, “Electrolyte for the high temperature fuel cell; experimental and theoretical studies of the perovskite LaAlO3,” J. Power Sources, 3 (1978) 67-80.
36. J. Mizusaki, I. Yasuda, J. Shimoyama, S. Yamauchi and K. Fueki, “Electrical conductivity, defect equilibrium and oxygen vacancy diffusion coefficient of La1-xCaxAlO3-δ single crystals,” J. Electrochem. Soc., 140[2] (1993) 467-471.
37. D. Lybye, F.W. Poulsen and M. Mogensen, “Conductivity of A- and B-site doped LaAlO3, LaGaO3, LaScO3 and LaInO3 perovskite,” Solid State Ionics, 128 (2000) 91-103.
38. J.Y. Park and G.M. Choi, “Electrical conductivity of Sr and Mg doped LaAlO3,” Solid State Ionics, 154-155 (2002) 535-540.
39. T.L. Nguyen, M. Dokiya, S. Wang, H. Tagawa and T. Hashimoto, “The effect of oxygen vacancy on the oxide ion mobility in LaAlO3-based oxide,” Solid State Ionics, 130 (2000) 229-241.
40. 李邦哲譯, “燃料電池,” 台灣經濟研究月刊, p72-74
41. 呂承頤, “燃料電池在太空之應用,” 能源、資源與環境, 3[1] (1990) 2-6.
42. D.H Archer, J.J. Alles, W.A. English, L. EliKan, E.F. Sverdrup, R.L.Zahradnik, in:Westinghouse Solid-Electrolyte Fuel Cell, Fuel Cell Systems, p332-342.
43. H. A. Harwig and A. G. Gerards, “The polymorphism of bismuth sesqui-oxide,” Thermochim. Acta, 28 (1979) 121–131.
44. K. Huang and J.B. Goodenough, “A solid oxide fuel cell based on Sr- and Mg-doped LaGaO3 electrolyte：the role of a rare-earth oxide buffer,” J. Alloy Comp., 303-304 (2004) 454-464.
45. T. Ishihara, M. Ando, M. Enoki and Y. Takita, “Oxide ion conductivity in La(Sr)Ga(Fe,Mg)O3 and its application for solid oxide fuel cells,” J. Alloy Comp., 408-412 (2004) 507-511.
46. V.P. Gorelov, D.I. Bronin, J.V. Sokolova, H. Nafe and F. Aldinger, “The effect of doping and processing conductions on properties of La1-xSrxGa1-yMgyO3-δ,” J. Eur. Ceram. Soc., 21 (2001) 2311-2317.
47. S. Kim, M.C. Chun, K.T. Lee and H.L. Lee, “Oxygen-ion conductivity of BaO- and MgO-doped LaGaO3 electrolytes,” J. Power Sources, 93 (2001) 279-284.
48. S.M. Choi, K.T. Lee S. Kim, M.C. Chun and H.L. Lee, “Oxygen ion conductivity and cell performance of La0.9Ba0.1Ga1-xMgxO3-δ electrolyte,” Solid State Ionics, 131 (2000) 221-228.
49. P. Sarkar and P.S. Nicholson, “Electrophoretic deposition (EPD) : Mechanism, kinetics, and application to ceramics,” J. Am. Ceram. Soc., 79[8] (1996) 1987-2002.
50. I. Zhitomirsky, “Cathodic electrodeposition of ceramic and organoceramic materials. Fundamental aspects,” Adv. Colloid Interf. Sci., 97 (2002) 279-317.
51. G.W. Morey, “Hydrothermal synthesis,” J. Am. Ceram. Soc., 36[9] (1953) 279-285.
52. W.J. Dawson, “Hydrothermal synthesis of advanced ceramic powders,” Ceram. Bull., 67[10] (1988) 1673-1678.
53. S. Wada, T. Suzuki and T. Noma, “Preparation of barium titanate fine particles by hydrothermal method and their characterization,” J. Ceram. Soc. Jpn., 103[12] (1995) 1220-1227.
54. A. Chittofratt and E. Matijevic, “Uniform particles of zinc-oxide of different morphologies,” Colloids Surf., 48[1] (1990) 65-78.
55. R. D. Shannon, “Revised effective ionic radii and systematic studies of interatomic distances in halides and chalcogenides,” Acta Cryst., A32 (1976) 751-767.
56. R.J.D Tilley, Deffect Crystal Chemistry and its Applications, pp9-11, Blackie, New York 1987.
57. A.F. Sammells, R.L. Cook, J.H. White, J.J. Osborne and R.C. MacDuff, “Rational selection of advanced solid electrolytes for intermediate temperature fuel cells,” Solid State Ionics, 52 (1992) 111-123.
58. J.A. Kilner, “A study of oxygen ion conductivity in doped non-stoichiometric oxides,” Solid State Ionics, 6 (1982) 237-252.
59. R.L. Cook, A.F. Sammells, “On the systematic selection of perovskite Solid electrolytes for intermediate temperature fuel cells,” Solid State Ionics, 45 (1991) 311-321.
60. E.J.W. Verwey, J.T.G. Overbeek, Theory of the Stability of Lyophobic Colloids, Elsevier, Amsterdam, 1948.
61. S. Okumuta, T. Tsukamoto and N, Koura, “Fabrication of ferroelectronic BaTiO3 films by electrophoretic deposition,” Jpn. J. Appl. Phys., 32 (1993) 4182-4185.
62. F.L. Chen and M.L. Liu, “Preparation of yttria-stabilized zirconia (YSZ) films on La0.85Sr0.15MnO3 (LSM) and LSM–YSZ substrates using an electrophoretic deposition (EPD) process” J. Eur. Ceram. Soc., 21[2] (2001) 127-134.
63. L. Vasylechko, A. Matkovski, A. Suchocki, D. Savytskii and I. Syvorotka, “Crystal structure of LaGaO3 and (La,Gd)GaO3 solid solutions,” J. Alloy Comp., 286 (1999) 213-218.
64. S. Geller and V. B. Bala, “Crystallographic studies of perovskite-like compounds. II. rare earth aluminates,” Acta Cryst., 9 (1956) 1019-1025.
65. P. R. Slater, J. T. S. Irvine, T. Ishihara and Y. Takita, “High-Temperature Powder Neutron Diffraction Study of the Oxide Ion Conductor La0.9Sr0.1Ga0.8Mg0.2O2.85,” J. Solid State Chem., 139[3] (1998) 135-140.
66 M. Hrovat, A. Ahmad-Khanlou, Z. Samardzija and J. Holc, “Interactions between lanthanum gallate based solid electrolyte and Ceria,” Mat. Res. Bull., 34[12-13] (1999) 2027-2034.
67 X. Zhang, S. Ohara, R. Maric, H. Okawa, T. Fukui, H. Yoshida, T. Inagaki and K. Miura, “Interface reactions in the NiO-SDC-LSGM system,” Solid State Ionics, 133 (2000) 153-160.
68 P. Huang, A. Horky and A. Petric, “Interfacial reaction between nickel oxide and lanthanum gallate during sintering and its effect on conductivity,” J. Am. Ceram. Soc., 82[9] (1999) 2402-2406.
69 K. Yamahara, C.P. Jacobson, S.J. Visco, L.C. De Jonghe, “Catalyst-infiltrated supporting cathode for thin-film SOFCs,” Solid State Ionics, 176 (2005) 451-456.
70 T.J. Armstrong and A.V. Virkar, “Performance of solid oxide fuel cells with LSGM-LSM composite cathodes,” J. Electrochem. Soc., 149[12] (2002) A1565-1571.
71 T. Ishihara, K. Shimose, T. Kudo, H. Nishiguchi, T. Akbay and Y. Takita, “Preparation of yttria-stabilized zirconia thin films on strontium-doped LaMnO3 cathode substrates via electrophoretic deposition for solid oxide fuel cells” J. Am. Ceram. Soc., 83[8] (2000) 1921-1927.
72 I. Zhitomirsky, “Cathodic electrodeposition of ceramic and organoceramic materials. fundamental aspects,” Adv. Colloid Interf. Sci., 97 (2002) 277-315.
73 K.Q. Huang and J.B. Goodenough, “Wet chemical synthesis of Sr- and Mg-doped LaGaO3, a perovskite-type oxide-ion conductor,” J. Solid State Chem., 136 (1998) 274-283.
74 A.C. Tas, P.J. Majewski and F. Aldinger, “Preparation of strontium- and zinc-doped LaGaO3 powders via precipitation in the presence of urea and/or enzyme urease,” J. Am. Ceram. Soc., 85 [6] (2002) 1414-1420.
75 R.E.S II, C. Habeger, A. Rabinovich and J.H. Adair, “Enzyme-catalyzed inorganic precipitation of aluminum basic sulfate,” J. Am. Ceram. Soc., 81 [5] (1998) 1377-1379.