KnE Materials Science | Sino-Russian ASRTU Conference Alternative Energy: Materials, Technologies, and Devices | pages: 1–7

, , , , , and

1. Introduction

One of the key positions of modern materials science is the research and development of solid oxide fuel cells and their components, including electrolytic membrane materials. It is necessary to find inexpensive and technological solid electrolyte with high conductivity and stability at high temperature, in oxidizing and reducing atmosphere. Medium temperatures are the most optimal region in terms of energy costs. Prospective ionic conductors for this temperature range are proton electrolytes based on the complex oxides.

The most studied method for modification of their structure and optimization of physicochemical properties is a homogeneous cationic doping [1–5]. However, the homogeneous anionic doping is a new promising way for the obtaining of new materials with improved properties. Earlier, we have reported a new route for increasing oxygen-ion and proton conductivities by F - -doping of brownmillerite Ba 2 In 2 O 5 [6]. It has been proved that small F - -concentrations can improve the oxide-ion (mixed anion effect) and the proton conductivities. The other prospective method of improving transport properties is a heterogeneous doping. The composites based on Ba 2 In 2 O 5 with chemically inert Ba 2 InNbO 6 oxide phase as a heterogeneous dopant demonstrate significant increase of conductivity level. The maximum conductivity corresponds to the ratio of the components 0.7:0.3 [7]. In this work the possibility of application of simultaneous homogeneous and heterogeneous doping has been described for the first time. The composite 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 has been chosen for the investigation.

2. Methods

We used in situ solid-state method for preparing the composite. This method consisted in simultaneous synthesis of the components from starting materials in the same reaction mixture:

white1.93 BaCO 3+0.85 In 2O3+0.15 Nb 2O5+0.035 BaF 2twhite0.7 Ba 1.95 In 2O4.9F0.1·0.3 Ba 2 InNbO 6+1.93 CO 2

(1) using temperature treatments 800–1300 C, six stage 24h each.

The X-ray powder diffraction (XRD) measurements were made on a Bruker Advance D8 diffractometer with Cu K α radiation. The crystal structure of the sample was determined through Rietveld refinement using FULLPROF software.

The surface morphology and local chemical composition were studied using a workstation AURIGA CrossBeam (Carl Zeiss NTS) and JEOL JSM 6390 LA scanning electron microscope with console JEOL JED-2300. The detection limit at ordinary energies (5–20 kV) was 0.5 at.%; the concentration measurement error was ± 2%.

Thermogravimetric analysis was carried out on STA (Simultaneous Thermal Analyzer) 409 PC analyzer (Netzsch) coupled with a quadrupole mass spectrometer QMS 403 C Aëolos (Netzsch). For the preparation of hydrated forms of the specimens, the powder samples were hydrated at slow cooling from 900 to 200 C (1 C/min) under a flow of wet air (pH 2 O = 2·10 -2 atm). The cooling was performed to a temperature not lower than 200 C to avoid the appearance of adsorbed water. The hydrated forms of the samples were heated at the rate of 10 C/min in a corundum crucible under a flow of argon.

The ceramics used for the electrical measurements were prepared by pressing disk-shaped samples at 250–300 MPa and sintering them at 1300 C for 24h in dry air. After polishing, the platinum paste electrodes were applied from both sides of the samples by painting and fired at 900 C for 3h. The ac conductivity of the samples (2-probe method) was measured using a Z-1000P (Elins) impedance spectrometer within the frequency range of 1-10 6 Hz. The conductivity measurements were carried out under dry and wet air varying the temperature and partial oxygen pressure pO 2 . The bulk resistance was calculated from a complex impedance plot using the Zview software fitting. The `wet' air was obtained by bubbling the gas at room temperature first through distilled water and then through the saturated solution of KBr (pH 2 O = 2·10 -2 atm). The `dry' air was produced by flowing the gas through P 2 O 5 (pH 2 O = 3.5·10 -5 atm). The humidity of gases was measured by H 2 O-sensor (`Honeywell' HIH-3610).

3. Results

According to XRD analysis, the sample contained two phases – cubic perovskite type Ba 2 InNbO 6 phase (Pm3m space group) and brownmillerite type Ba 1.95 In 2 O 4.9 F 0.1 phase (I4cm space group) with partial disordering of oxygen vacancies. The lattice parameters were a = 4.142 Å for Ba 2 InNbO 6 and a = 5.950(2) Å, c = 16.813(9) Å for Ba 1.95 In 2 O 4.9 F 0.1 . They were in a good agreement with previously reported data [7]. XRD-pattern for 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 refined by Rietveld analysis is presented in Figure 1.

Figure 1

XRD patterns of 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 . At the bottom of the figure – the difference between the experimental data and the calculated ones after refinement. Vertical bars show the Bragg angle positions.


The morphology of the samples was studied by scanning electron microscopy (SEM) (Figure 2). It can be seen for individual phases Ba 1.95 In 2 O 4.9 F 0.1 (Figure 2(a)) and Ba 2 InNbO 6 (Figure 2(b)) and for composite system (Figure 2(c)) that the grain size was approximately 5–10 μm and the grain boundaries were clean. The microelement analysis showed the presence of all main elements in the samples.

Figure 2

SEM image of individual phases Ba 1.95 In 2 O 4.9 F 0.1 (a), Ba 2 InNbO 6 (b), and composite system 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 (c).


Thermal analysis of the composite system showed that the composite changed mass at temperatures 300–500 C in wet atmosphere (pH 2 O = 2 · 10 -2 atm), which corresponded to the processes of removing water molecules (Figure 3). The maximal water uptake for composite system is proportional to the content of the phase Ba 1.95 In 2 O 4.9 F 0.1 with incompletion in the oxygen sublattice and is 0.60 mole H 2 O per formula 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3 Ba 2 InNbO 6 . The Ba 2 InNbO 6 phase is nominally complete in the oxygen sublattice and is capable of absorbing only small amounts of water due to an insignificant change in stoichiometry during the synthesis. Thus, the main amounts of proton defects are concentrated in the grains of the phase Ba 1.95 In 2 O 4.9 F 0.1 .

Figure 3

Thermogravimetry and mass-spectra data for hydrated sample 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 .


The conductivity measurements were carried out under dry (pH 2 O = 3.5·10 -5 atm) and wet (pH 2 O = 2·10 -2 atm) air by varying the temperature (250–1000 C) (Figure 4). The conductivity values of composite system 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3 Ba 2 InNbO 6 are significantly higher than those for both undoped Ba 2 In 2 O 5 composition and F-doped Ba 1.95 In 2 O 4.9 F 0.1 one in the whole temperature range. The increasing in conductivity under wet air for the composite proves the ability of the sample to the proton transfer.

Figure 4

Electric conductivity of Ba 2 In 2 O 5 [6], Ba 1.95 In 2 O 4.9 F 0.1 [6] and composite system 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 .


4. Conclusion

In this article, the possibility of application of simultaneous homogeneous and heterogeneous doping has been described for the first time. The composite 0.7Ba 1.95 In 2 O 4.9 F 0.1· 0.3Ba 2 InNbO 6 has been obtained by in situ solid-state method. It has been proved that composite sample is capable for water uptake and for proton transfer. The increasing in the conductivity values for the composite sample comparing with conductivity for the individual phases allows concluding that simultaneous homogeneous and heterogeneous doping is prospective method for obtaining high-conductive proton electrolytes.


This work was supported in parts by the Ministry of Education and Science of the Russian Federation (State Task 4.2288.2017) and by Act 211 Government of the Russian Federation, agreement 02.A03.21.0006. The equipment of the Ural Center for Shared Use `Modern nanotechnology' SNSM UrFU was used.



Yao T., Uchimoto Y., Kinuhata M., Inagaki T., Yoshida H., Crystal structure of Ga-doped Ba2In2O5 and its oxide ion conductivity, Solid State Ionics, Year: 2000, Volume: 132, Issue: 3, Page: 189-198. DOI: 10.1016/S0167-2738(00)00658-5


Kakinuma K., Yamamura H., Haneda H., Atake T., Oxide-ion conductivity of (Ba1-xLax)2In2O5+x system based on brownmillerite structure, Solid State Ionics, Year: 2001, Volume: 140, Issue: 3-4, Page: 301-306. DOI: 10.1016/S0167-2738(01)00853-0


Mitome M., Okamoto M., Bando Y., Yamamura H., Structure analysis of Ba2In2O5 and related compounds by electron microscopy, Journal of Vacuum Science & Technology B, Year: 2001, Volume: 19, Issue: 6, Page: 2284-2288. DOI: 10.1116/1.1421566


Quarez E., Noirault S., Caldes M. T., Joubert O., Water incorporation and proton conductivity in titanium substituted barium indate, Journal of Power Sources, Year: 2010, Volume: 195, Issue: 4, Page: 1136-1141. DOI: 10.1016/j.jpowsour.2009.08.086


Jarry A., Quarez E., Joubert O., Tailoring conductivity properties of chemically stable BaIn 1 - X - yTixZryO 2.5 + (x + y)/2 - N(OH)2n electrolytes for proton conducting fuel cells, Solid State Ionics, Year: 2014, Volume: 256, Page: 76-82. DOI: 10.1016/j.ssi.2013.12.012


Animitsa I., Tarasova N., Filinkova Y., Electrical properties of the fluorine-doped Ba 2In 2O 5, Solid State Ionics, Year: 2012, Volume: 207, Page: 29-37. DOI: 10.1016/j.ssi.2011.11.015


Alyabysheva I. V., Kochetova N. A., Matveev E. S., Baldina L. I., Animitsa I. E., Stabilizing a disordered structural modification of barium indate by means of heterogenous doping, Bulletin of the Russian Academy of Sciences, Physics, Year: 2017, Volume: 81, Issue: 3, Page: 384-386. DOI: 10.3103/S1062873817030030



  • Downloads 13
  • Views 151



ISSN: 2519-1438