Method of producing an electrode layer on a solid oxide electrolyte of a solid state fuel cell

BACKGROUND OF THE INVENTION
1. Field of the Invention
This is a 371 of PCT/DK94/00304 filed on Aug. 08, 1994.
The present invention relates to a method of producing an electrode layer on, for instance, a solid electrolyte of a solid state fuel cell, where the electrode material is of the type La.sub.x Ca.sub.y CrO.sub.3, and X+Y.gtoreq.1 and Y>0, the electrode material being subjected to a sintering.
2. Description of the Related Art
The sintering must be as efficient as possible. In addition, it must be possible to carry out cosintering with other materials, such as YSZ. The sinterings were originally carried out at relatively high temperatures. It was discovered that it was possible to lower the temperature by adding La and Ca in excess to the composition, whereby the fluid and spreading characteristics of an intrinsic wet phase and consequently the densification are improved. However, the resulting stability may be deteriorated, and the excess ingredients may react with the adjacent materials which presents a drawback for instance in connection with SOFC (Solid oxide fuel cell) cells.
SUMMARY OF THE INVENTION
An object of the invention is to provide a method of producing all electrode material with improved sintering properties, the risk of reactions with the adjacent materials simultaneously being reduced or eliminated.
The method according to the invention is characterised by adding a few mol %, preferably 1 10 mol %, of vanadium to the electrode material, whereby the resulting densities turned out to be considerably improved. A cosintering with YSZ indicates that it is possible to cosiniter with YSZ without involving reactions with YSZ.
According to the invention it is particularly advantageous to add 1 to 2 mol % of vanadium, whereby the density can be increased to 96%.
The method according to the invention may for instance be used for producing a heat resistance.
As an alternative, the method according to the invention can be used for producing a sensor electrode, such as an oxygen sensor electrode.

BRIEF DESCRIPTION OF THE DRAWINGS
FIG. 1 is a photograph of an unpolished surface of a material according to the present invention;
FIG. 2 is a photograph of a magnified view of the material in FIG. 1;
FIG. 3a is a photograph of a magnified view of LCC65 particles;
FIG. 3b is a photograph of a magnified view of the material of FIG. 3a after coating and calcination;
FIG. 4 is a photograph of an unpolished surface of a material according to the present invention;
FIG. 5 is a graph of an x-ray diffraction pattern of a material according to the present invention;
FIG. 6 is a series of graphs of a high temperature x-ray diffraction pattern of the material of the invention; and
FIG. 7 is a series of graphs of a high temperature x-ray diffraction study for another material according to the invention.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
A ceramic La.sub.x Ca.sub.y CrO.sub.3 can be used as an electric conductor at high temperatures. The electrical conductivity thereof at 1,000.degree. C. is 5 to 50 S/cm at an oxygen partial pressure P.sub.02 of 10.sup.-18 to 1 atm. This material can be used as a heating unit in an oven, as connectors and anodes in SOFC, and as electrodes for zirconia-based O.sub.2 sensors.
One of the greatest challenges of using La.sub.x Ca.sub.y CrO.sub.3 is to sinter in air at moderate temperatures of less than 1,500.degree. C. Chromium oxides (CrO.sub..delta., where .delta.=2 to 3) volatilize from La.sub.x Ca.sub.y CrO.sub.3 and result in concentrating particle coarsening mechanisms. Alkaline earth doped LaCrO.sub.3 was originally sintered at 1,700.degree. C. in a reducing atmosphere (P.sub.02 =10.sup.-11 atm) to lower the vapour pressure of CrO.sub..delta.. This method provided densities of more than 95% of the theoretically possible densities.
Later it was found that such densities could be achieved in air at 1,300.degree. to 1,500.degree. C. by synthesizing La.sub.x Ca.sub.y CrO.sub.3 with y.gtoreq.0.25 and x+y>1 or by creating an excess of A sites, reference being made to the crystal structure of ABO.sub.3 perovskite. Such compositions release extra Ca into a temporarily exsolved liquid phase Ca.sub.1+.delta. --CrO.sub.4 used for promoting the sintering. The ability of the Ca.sub.1+.delta. CrO.sub.4 to promote a sintering is increased with an increasing excess of A site ions. The densification proceeds as a consequence of a mass transport of the ingredients through the liquid, which promotes the grain growth and the filling of intergranular pores. By the achievement of high densities it is assumed that Ca.sub.1+.delta. CrO.sub.4 is redissolved into La.sub.x Ca.sub.y CrO.sub.3 to form a single phase solid solution.
Some problems arise by this sintering method. It is also difficult to form a solid solution with La.sub.x Ca.sub.y CrO.sub.3 by substituting Ca for La in excess of 25 mol %. Thus, the Ca.sub.1+.delta. CrO.sub.4 is reactive towards corresponding materials during sintering and subsequent heating cycles. Secondary phases develop from interfacial reactions which are less chemically stable and have lower electric conductivities. These ultimately degrade the desired properties of La.sub.x Ca.sub.y CrO.sub.3.
These problems can be minimized by reducing the total amount of Ca substituted into La.sub.x Ca.sub.y CrO.sub.3 to less than 25% and by keeping the excess of A sites near the stoichiometric limit (i.e. x+y.apprxeq.1). When these precautions have been taken, the sinterability of La.sub.x Ca.sub.y CrO.sub.3 is reduced and it is again difficult to obtain a high density.
A demand exists therefore, for a method of reducing the calcium reactivity while maintaining a high sinterability together with the chemical and electrical properties of La.sub.x Ca.sub.y CrO.sub.3. By adding V to La.sub.x Ca.sub.y CrO.sub.3, the sinterability thereof is improved without requiring an excess of A site cations or an excess of Ca. The chemical stability and the electrical properties and a low V doping (of <5 mol %) have been found to be similar to undoped La.sub.x Ca.sub.y CrO.sub.3.
Powder compositions were prepared by two different processes. Both are polymer pyrolysis techniques including a dissolving of metal nitrates in water and an adding of chelating agents to form a polymer precursor. Water is evaporated from the precursor solution to form a gel and the gel is pyrolysed to remove organic ingredients, which results in a homogenous mixture of metal oxides.
The liquid mixture process (LM) uses ethylene glycol and citric acid as chelating agents, cf. L. Tai, P. Lessing "Modified resin-intermediate processing of perovskite powders: Part II. Processing for fine, nonagglomerated Sr-doped lanthanum chromite powders", J. Mater. Res., 7 �2!, 511-519 (1992). The pyrolysis occurs at a slow rate (for 1 to 3 hours) and at low temperatures of about 300.degree. C. This technique was chosen so that V could be added into the initial synthesis of La.sub.x Ca.sub.y CrO.sub.3 without risking a volatilization during the polymer pyrolysis.
Standardized aqueous solutions of La, Ca, and Cr nitrates were mixed in a glass beaker with ethylene glycol and citric acid so that the molar ratios of the final La.sub.x Ca.sub.y CrO.sub.3 composition/ethylene glycol/citric acid=1:1:1.
Vanadium oxide V.sub.2 O.sub.5 of a purity of 99.9% was used as V-source. Since the pentaoxide is difficult to dissolve in an aqueous solution, a soluble VO.sub..delta. -citric acid complex was prepared by mixing V.sub.2 O.sub.5 and citric acid in deionized water with a weight ratio of oxide to acid to water of 1:4:20 and by heating to 80.degree. to 90.degree. C. The complex reaction was completed at the formation of a clear blue solution. This colour is an indication of oxovanadium (the IV-compound, cf. F. A. Cotton and G. W. Wilkinson advanced inorganic chemistry a comprehensive text. Interscience Publishers, New York 1972 p 825), although the structure of the VO.sub..delta. -citric acid complex has not been determined. This solution was added to the solution of chelated La, Ca, and Cr ions or used as a coating as described below.
The LM solution containing the VO.sub.67 -citric acid complex was heated on a hot plate to about 80.degree. C. to remove water and to form a polymeric gel. After the formation of the gel, the temperature of the hot plate was raised to about 300.degree. C., and the gel was polymerized in an amorphous char. The charge was ball milled in ethanol for 4 hours, dried and calcined at 750.degree. C. for 4 hours to obtain a crystalline phase and to remove residual carbon.
The Glycine process is described by L. A. Chick, J. L. Bates, L. R. Pederson and H. E. Kissinger in the paper "Synthesis of Air-Sinterable Lanthanum Chromite Powders", p 170-187, in Proceedings of the First International Symposium on Solid Oxide Fuel Cells, vol. 89-11, edited by S. C. Singhal (Pennington N.J.: The Electrochemical Society, Inc. 1989). This process uses glycine as a chelating agent and a fuel for pyrolysis. The pyrolysis occurs in 2 to 3 sec and at temperatures exceeding 1,000.degree. C. The powder resulting from this process is crystalline, nanometer sized (.about.50 nm), weakly agglomerated and free of organic residues. The amount of glycine used is determined by the amount of nitrate in the solution and the amount of metals which must be chelated. A glycine:nitrate ratio G:N is first calculated to obtain the most efficient combustion. By way of tests it was determined that a G:M ratio of at least 1.5 is needed to chelate all the metals. Extra glycine and HNO.sub.3 can be added to the solution to satisfy both requirements. At the proper value G:N, a vigorous reaction occurs which obtains peak flame temperatures of >1,000.degree. C. Since VO.sub.2 and V.sub.2 O.sub.5 have high vapour pressures at these temperatures, it was speculated that V might be lost during the synthesis. La.sub.x Ca.sub.y CrO.sub.3 was consequently synthesized with and without V to determine the difference in the sinterability. Aqueous La, Ca, and Cr nitrate solutions, the VO.sub..delta. -citric acid complex, and glycine were balanced in a tall 2,000 ml beaker, where G:N=0.5 and G:M=1.5 to 1.7. A 40 mesh screen of steel was placed over the top of the beaker to capture fine solid particles during the pyrolysis. The batch size should not exceed 0.05 mol of perovskite to contain the powder in the beaker during the pyrolysis. The mixture was heated in a fume hood to remove water, being careful not to exceed 200.degree. C. to avoid premature ignition. After formation of a syrupy gel, the solution was heated to 300.degree. C. and pyrolysed. After pyrolysis, the powder was subjected to a dry ball milling to break up agglomerates and calcined into air as specified in Table I to coarsen the powders.
Calcined powder not synthesized with V was coated with the VO.sub..delta. -citric acid solution. The solution was added in desired doping amounts to a slurry of La.sub.x Ca.sub.y CrO.sub.3 in ethanol.
After a suitable mixing, the slurry was dried and recalcined at 500.degree. to 600.degree. C. to remove organic substances.
Specimens were formed by uniaxially pressing powders into disks or bars at 150 to 200 MPa. Sintering temperatures and times are summarized in Table I.
The electrical conductivity was measured for La.sub.0.76 Ca.sub.0.24 CrV.sub.0.02 O.sub.3 at 1,000.degree. C. in air and at 10.sup.-16 atm O.sub.2 using a four point measuring technique described by H. Toftegaard and M. Mogensen in the paper "Electrical Conductivity of LSM", unpublished departmental report: BC-103, Ris.o slashed. National Laboratory, Roskilde DK, December 1992. The current source is specially designed, and the device for measuring the electrical voltages was a HP3421A data acquisition and control unit.
Manually cast foils were made from the composition La.sub.0.76 Ca.sub.0.26 CrO.sub.3 +2 mol % V. Powder slurries were prepared and cast on a glass substrate into a tape of 9.multidot.60.multidot.0.03 cm, using a tape casting technique developed by Ris.o slashed., cf. the paper by C. Bagger "Improved Production Methods for YSZ Electrolyte and Ni--YSZ Anode for SOFC" Extended abstract of poster, presented at the 1992 Fuel Cell Seminar, Tucson, Ariz., Nov. 29 to Dec. 2, 1992. The chromate tapes were laminated with a green 8 mol % YSZ tape by painting and corresponding surfaces of the tapes with ethanol by passing the laminates through a roller mill. The laminates were placed between fibrous alumina plates to prevent curling and sintered in air at 1,300.degree. C. for 6 hours.
A spray coating slurry was prepared containing 12% by weight of La.sub.0.8 Ca.sub.0.2 Cr.sub.0.98 V.sub.0.02 O.sub.3 (calcined at 1,000.degree. C. for 2 hours), 12% by weight "as synthesized" powder (from the same batch), 56% by weight of ethanol, 4% by weight of polyvinyl pyrrolidone solution (PVP) �0.53 g PVP/g 66% by volume of methylethylketone, 33% by volume of ethanol!, and 16% by weight of 3 mol % Y.sub.2 O.sub.3 partially stabilized ytterbium (TZ-3Y from Tosoh Corp. Tokyo 170, Japan) (PSZ). The first three ingredients and half the PVP were ball milled for 24 hours. PSZ and the remaining PVP were then added to the slurry, and the entire mixture was again ball milled for 24 hours. After milling, the slurry was sprayed onto sintered YSZ tapes with an airbrush and dried for 15 minutes. The coated YSZ plates were then sintered at 1,300.degree. C. for two hours.
TABLE I______________________________________Sintering data for La.sub.x Ca.sub.y CrO.sub.3 + VLa.sub.x Ca.sub.y - Powder SynthesisCrO.sub.3 + V Calcination Condi- Theoreti-Composi- tions and V Addition Sintering Density cal Den-tion Method temp/time (g/cm.sup.3) sity______________________________________La.sub.0.76 - Glycine- 1350.degree. C. 4.45 72%Ca.sub.0.26 C- 1200.degree. C./2 h /3 hrO.sub.3*La.sub.0.76 - Glycine- 1300.degree. C. 6.02 96%Ca.sub.0.26 C- 1200.degree. C./2 h /2 hrO.sub.3 + 2 VO.sub..delta. -citric acidmol % V coatedLa.sub.0.76 LM-750.degree. C./4 h 1300.degree. C. 5.68 91%Ca.sub.0.24 - V doped /2 hCrV.sub.0.02 O.sub.3La.sub.0.8 Glycine- 1450.degree. C. 4.37 69%Ca.sub.0.2 CrO.sub.3 1200.degree. C./2 h /8 hLa.sub.0.8 Glycine- 1450.degree. C. 5.85 92%Ca.sub.0.2 CrO.sub.3 1200.degree. C./2 h /8 h+ 1 mol % VO.sub..delta. -citric acidV coated*La.sub.0.8 - Glycine- 1450.degree. C. 5.95 94%Ca.sub.0.2 Cr- 1000.degree. C./8 h /8 h.sub.0.98 V V doped.sub.0.02 O.sub.3La.sub.0.8 Ca.sub.0.2 Glycine- 1350.degree. C. 5.96 94%Cr.sub.0.95 V- 1000.degree. C./2 h /2 h.sub.0.10 O.sub.3 V doped______________________________________
The sintering densities are summarized in Table I. In general, the sintering density of La.sub.x Ca.sub.y CrO.sub.3 has been improved from less than 75% to more than 90% of the theoretical value by the addition of V. The temperature and the necessary times needed to obtain a high density depend on the total amount of Ca added to the V doped composition. Ca additions of 24 to 26 mol % required 1,300.degree. C. and 2 hours for achieving high densities, whereas additions of 20 mol % Ca required 1,450.degree. C. and 8 hours. The temperature and the time were, however, reduced to 1,350.degree. C. and 2 hours for the 20 mol % Ca composition when the V content was increased to a total of 10 mol % with an excess of 5 mol %.
The compositions indicated by a * are stoichiometric with respect to the A and B cations (i.e. A/B=1). It is assumed that V substitutes on the B site since V.sup.3+ and V.sup.4+ have ionic radii similar to Cr.sup.3+ and Cr.sup.4+. This is the major advantage of adding V to La.sub.x Ca.sub.y CrO.sub.3. Previous low temperature sintering compositions of La.sub.x Ca.sub.y CrO.sub.3 required an excess of A cations (x+y>1) to achieve high sintering densities. Stoichiometric La.sub.x Ca.sub.y CrO.sub.3 is preferred because the reactivity of Ca in the liquid phase is reduced and a single phase is obtained after sintering.
The sinterability of powders prepared by means of LM, glycine or VO.sub..delta. -citric acid coating processes are all comparable. Apparently, V does not evaporate at high temperatures as was supposed, but it is incorporated in the La.sub.x Ca.sub.y CrO.sub.3 system. Vanadium can therefore be added to La.sub.x Ca.sub.y CrO.sub.3 at various stages of powder synthesis and can even be used to balance the stoichiometry in existing La.sub.x Ca.sub.y CrO.sub.3 powders.
Table II shows the electrical conductivity values of La.sub.0.76 Ca.sub.0.24 CrV.sub.0.01 O.sub.3 at 100.degree. C. in air and under reducing conditions. These values lie within the conductivity range of similar La.sub.x Ca.sub.y CrVO.sub.3 compositions developed by Ris.o slashed..
TABLE II______________________________________Electrical conductivities of La.sub.0.76 Ca.sub.0.24 CrV.sub.0.01 O.sub.3at 100.degree. C.Atmospheric gases/Po.sub.2 (atm) Conductivity (S/cm)______________________________________air/0.21 309%H.sub.2,3%H.sub.2 O,91%N.sub.2 /3.2 .times. 10.sup.-16 12______________________________________
Laminates of La.sub.0.76 Ca.sub.0.26 CrO.sub.3 +2 mol % V and /YSZ demonstrated good bonding at their interface after sintering. The La.sub.0.80 Ca.sub.0.20 Cr.sub.0.98 V.sub.0.02 O.sub.3 -PSZ spray coated mixture showed good adherence to the YSZ surface. These preliminary tests indicate that La.sub.x Ca.sub.y CrO.sub.3 can be attached to YSZ by way of cosintering and are used to form electrodes or interconnectors for SOFC and in connection with YSZ oxygen sensors.
Thus, vanadium additions of 1 to 2 mol % have shown to significantly improve the sinterability of La.sub.x Ca.sub.y CrO.sub.3 without requiring the addition of an excess of A site cations or of extra Ca. The electrical conductivity of V-doped La.sub.x Ca.sub.y CrO.sub.3 was unchanged compared to undoped compositions. Preliminary tests indicate the possibility of bonding La.sub.x Ca.sub.y CrO.sub.3 to YSZ by cosintering or spray coating techniques. It is believed that an addition of V can further improve the sinterability of other rare-earth/chromium based materials such as Y.sub.x Ca.sub.y CrO.sub.3, LaCr.sub.x Mg.sub.y O.sub.3, and La.sub.x Sr.sub.y CrO.sub.3.
Additional investigation into the (La,M)(Cr,V)O.sub.3 perovskite system has sought to gain a better understanding of the effect of V as a sintering aid. More (La,Ca)(Cr,V)O.sub.3 and (La,Sr)(Cr,V)O.sub.3 batches were synthesized and sintered to further verify the effect of V on the sinterability of these systems. Microscopic and phase analyses show that a liquid phase forms which is based on the CaO--Cr.sub.2 O.sub.3 phase system for (La,Ca)CrO.sub.3 compositions. This liquid is found to contain V and it is believed that the V modifies the sintering characteristics. A similar liquid was observed in the (La,Sr)CrO.sub.3 compositions based on SrCrO.sub.4 from the SrO--Cr.sub.2 O.sub.3 phase system.
Additional electrical measurements show that the addition of V has little effect on the conductivity of (La,M)CrO.sub.3 (M=Ca,Sr) in air or under a reducting atmosphere.
Microscopic analysis
(La,Ca) (Cr,V)O.sub.3
Sintered specimens analyzed by SEM showed evidence of liquid phase sintering in (La,Ca)(Cr,V)O.sub.3. FIG. 1 shows an unpolished surface of La.sub.0.76 Ca.sub.0.26 CrO.sub.3 +2 at % V sintered at 1300.degree. C. for 2 h. The glassy striations on the surface of the (La,Ca)(Cr,V)O.sub.3 grains are typical of the liquid phase also found in the (La,Ca)CrO.sub.3 system. Elemental analysis of the liquid phase showed the presence of Ca,V and Cr. After the grains coalesced and the pores filled in, excess liquid segregated out of the grains to the free surface. A magnified view of the same specimen in FIG. 2 shows that the (La,Ca)(Cr,V)O.sub.3 grains have sintered to high density with 5-7 vol % porosity.
To investigate the nature of VO.sub.x coating, a microscopic study was made of LCC65 with and without the addition of the VO.sub.X -citric acid solution. In this case the VO.sub.x -citric acid solution was added to a stirred slurry of (La,Ca)CrO.sub.3 in ethanol. FIG. 3a shows LCC65 particles (without V), calcined at 1200.degree. C. for 2 h. The particle surfaces appear smooth with edges on the facets. FIG. 3b shows the same powder after it had been coated with the VO.sub.x -citric acid solution and calcined at 650.degree. C. to remove the organics. Here, the particle surfaces have a textured coating which is distributed throughout the bulk of the powder matric. Sintered bodies made from this powder revealed a uniform grain size as seen in FIG. 2.
(La,Sr) (Cr,V)O.sub.3
Microscopic analysis of (La,Sr)(Cr,V)O.sub.3 compositions showed uniform grain growth and high sintering density. FIG. 4 shows an unpolished surface of a pellet of La.sub.0.8 Sr.sub.0.2 Cr.sub.0.97 V.sub.0.03 O.sub.3 (DC27), calcined at 1000.degree. C./2 h and sintered at 1400.degree. C./2 h. SrCrO.sub.4 was identified by XRD (x-ray diffraction) as one of the a secondary phases forming in (La,Sr)(Cr,V)O.sub.3, below 1000.degree. C. Since the phase diagram of the SrO--Cr.sub.2 O.sub.3 system, cf. T. Negas and R. S. Roth, J.Res.Nat.Bur.Stand.Sect.A,73 �4! (1969) 433.34, shows that SrCrO.sub.4 melts between 1250.degree.-1285.degree. C., it is believed that a modification of this liquid phase also occurs in the (La,Sr)(Cr,V)O.sub.3 system and acts as a sintering aid. Possible remnants of a liquid phase can be seen between the grains in FIG. 4. Microscopic analysis of a similar specimen sintered at 1450.degree. C. for 2 h showed a molten phase on the free surface with an appearance similar to that found in the (La,Ca)(Cr,V)O.sub.3 specimens.
Phase analysis
X-ray diffraction was employed to identify secondary phases which exsolve from (La,M)(Cr,V)O.sub.3 at various temperatures during annealing and sintering. Diffraction patterns of (La,M)(Cr,V)O.sub.3 compositions, synthesized using the glycine process are characteristically single phase with broad peaks indicating submicron primary particle sizes. For example, FIG. 5 is a diffraction pattern of as-synthesized La.sub.0.8 Sr.sub.0.2 Cr.sub.0.98 V.sub.0.02 O.sub.3. It is believed that the apparent high solubility for foreign ions in LaCrO.sub.3 is caused by the high temperature of pyrolysis and rapid cooling of the resulting particles as they are discharged from the pyrolysis zone. The diffraction pattern of the as-synthesized powder changes according to temperature; when powders are heated above 400.degree. C., the diffraction peaks sharpen and secondary phases appear according to the equilibrium solubility of foreign ions in the host matrix.
In the (La,M)(Cr,V)O.sub.3 system, the secondary phases can ordinarily be identified between 20.degree.-36.degree.-2.theta. in the diffraction pattern. In both Sr and Ca doped (La,M)(Cr,V)O.sub.3, either LaVO.sub.4 or LaCrO.sub.4 or a solid solution of both form as a secondary phase at temperatures below 700.degree. C. The two compounds are isostructural, each having a monazite-type structure (space group: P2.sub.1 /n), and exhibit closely similar diffraction patterns, cf. LaCrO.sub.4, JCPDS Card # 36-93, Joint Committee on Powder Diffraction Standards, 1601 Park Lane, Swarthmore, Pa. 19081 (1986) and LaVO.sub.4, JCPDS Card # 25-427, Joint Committee on Powder Diffraction Standards, 1601 Park Lane, Swarthmore, Pa. 19081 (1975). Consequently, they are difficult to resolve from another using only XRD. But the present belief is that LaVO.sub.4 is the phase formed because these diffraction peaks are not seen in compositions not containing V; and LaVO.sub.4 is the most stable form of vanadates in air, cf. T. Nakamura, G. Petzow and L. Gaukler, Mat.Res.Bull., 14 (1979) 649-659. In contrast, LaCrO.sub.4 is relatively unstable in air under such conditions, cf. J. D. Carter, H. U. Anderson, M. G. Shumsky, "Structure and Phase Transformation of Lanthanum Chromate". Submitted for publication in the J.Mat.Sci. (1994).
When (La,M)(Cr,V)O.sub.3 compositions are heated above 700.degree. C., the LaVO.sub.4 disappears and either CaCrO.sub.4 of SrCrO.sub.4 takes its place as a secondary phase. FIG. 6 shows a high temperature XRD pattern of La.sub.0.8 Sr.sub.0.2 Cr.sub.0.97 V.sub.0.03 O.sub.3 (DC27) as it is heated to 1100.degree. C. and then cooled. The diffraction pattern of the as-synthesized powder shows broad peaks and a noisy background. No secondary phases are visible. At 500.degree. C., the peak widths have narrowed and LaVO.sub.4 peaks have become prominent. At 600.degree. C. the intensity of the LaVO.sub.4 peaks decrease by half and peaks from SrCrO.sub.4 become apparent. The crystal structure of SrCrO.sub.4 is also monazite-type, cf. SrCrO.sub.4, JCPDS Card # 35-743, Joint Committee on Powder Diffraction Standards, 1601 Park Lane, Swarthmore, Pa. 19081 (1985), but the XRD patterns of SrCrO.sub.4 and LaVO.sub.4 are more distinct. The peak intensities of SrCrO.sub.4 increase as the temperature is raised through 700.degree. and 800.degree. C., but at 1000.degree. C. they disappear. This could be the result of the formation of a liquid phase or because SrCrO.sub.4 has dissolved into the (La,Sr)(Cr,V)O.sub.3 matrix. Preliminary trials of differential thermal analysis (DTA) of La.sub.0.8 Sr.sub.0.2 Cr.sub.0.97 V.sub.0.03 O.sub.3 (DC33) gave no indication of melting taking place at this temperature, so it is believed that the SrCrO.sub.4 dissolves into (La,Sr)(Cr,V)O.sub.3 at this temperature for this composition.
A room temperature XRD study of annealed La.sub.0.8 Ca.sub.0.2 Cr.sub.0.97 V.sub.0.03 O.sub.3 (DC32) specimens (as-synthesized �600.degree. C.!, 700.degree., 800.degree., 900.degree., . . . 1300.degree. C. for 2 h) showed similar results (FIG. 7). The as-synthesized powder shows the peaks from the perovskite and secondary peaks of LaVO.sub.4. At 700.degree. and 800.degree. C. the intensity of the LaVO.sub.4 peaks decrease and the CaCrO.sub.4 phase becomes apparent. By 1000.degree. C. the CaCrO.sub.4 phase disappears and at 1100.degree. C. only peaks from the perovskite phase are discernible. It is known from DTA analysis that CaCrO.sub.4 melts near 1030.degree. C.; and the resulting liquid phase has been shown to aid in sintering (La,Ca)Cr O.sub.3, cf. J. D. Carter, M. M. Nasrallah, and H. U. Anderson, "Liquid Phase Behavior in Nonstoichiometric Calcium Doped Lanthanum Chromites". Submitted for publication in the J.Mat.Sci. (1994). The presence of V within the liquid phase is believed to enhance the sintering action of this liquid phase.
Electrical conductivity
Electrical conductivity measurements of (La,M)(Cr,V)O.sub.3 in air and in reducting atmosphere indicate that the conductivity is relatively unaffected by the V doping. Table III shows the electrical conductivity values of (La,M)(Cr,V)O.sub.3 and (La,Sr)CrO.sub.3 compositions. The conductivities lie within the range of values found in the literature, cf. N. Sakai, T. Kawada, H. Yokokawa, M. Dokiya and T. Iwata, "Sinterability and Electrical Conductivity of Calcium-Doped Lantahnum Chromites", J.Mater. Sci. 25, 4531-4534 (1990), I. Yasuda and T. Hikita, J. Electrochem. Soc., 140 �60! (1993) 1699-1704 and W. Schafer and R. Schmidberger, "Ca and Sr Doped LaCrO.sub.3 : Preparation, Properties and High Temperature Applications" pp. 1737-42 High Tech Ceramics. Edited by P. Vincenzini. (Amsterdam, Elsevier Science Publishers, 1987).
TABLE III______________________________________Electrical conductivities of (La,M)(Cr,V)O.sub.3 at 1000.degree. C. Conductivity (.OMEGA..sup.-1 cm.sup.-1) airlog 16 atm O.sub.2Compositionlog 0.68 atm O.sub.2 (10% H.sub.2 in N.sub.2) Ref.______________________________________La.sub.0.74 Ca.sub.0.36 CrO.sub.3 50 3 8La.sub.0.76 Ca.sub.0.26 CrO.sub.3 + 2 at 30 12 this% V studyLa.sub.0.8 Ca.sub.0.2 CrO.sub.3 40 18 9LA.sub.0.8 Ca.sub.0.2 Cr.sub.0.97 V.sub.0.03 O.sub.3 30 12 this studyLa.sub.0.8 Sr.sub.0.2 CrO.sub.3 31 -- 10La.sub.0.8 Sr.sub.0.2 Cr.sub.0.97 V.sub.0.03 O.sub.3 30 5 this study______________________________________
Continued studies on V doped (La,Ca)CrO.sub.3 and (La,Sr)CrO.sub.3 compositions show that sintering proceeds through a liquid phase sintering mechanism. Vanadium was seen to dissolve into the liquid phase and it is believed to enhance the ability of the Ca--Cr--O and the Sr--Cr--O liquid phase and it is believed to enhance the ability of the Ca--Cr--O and the Sr--Cr--O liquid phases to aid sintering. Electrical measurements showed that conductivities with respect to non V-doped compositions remained relatively constant.
Although other modifications and changes may be suggested by those skilled in the art, it is the intention of the inventor to embody within the patent warranted hereon all changes and modifications as reasonably and properly come within the scope of his contribution to the art.

Method of producing an electrode layer on a solid oxide electrolyte of a solid state fuel cell

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