Next Article in Journal
Bulk Density Homogenization and Impact Initiation Characteristics of Porous PTFE/Al/W Reactive Materials
Previous Article in Journal
Recycling of a Concrete Pavement after over 80 Years in Service
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Materials
Volume 13
Issue 10
10.3390/ma13102267
materials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Molten Salt Synthesis of High-Performance, Nanostructured La0.6Sr0.4FeO3−δ Oxygen Electrode of a Reversible Solid Oxide Cell

by
Xiaodong Zuo
1,2,†,
Zhiyi Chen
3,†,
Chengzhi Guan
2,4,*,
Kongfa Chen
3,*,
Sanzhao Song
2,
Guoping Xiao
2,4,
Yuepeng Pang
1,* and
Jian-Qiang Wang
2,4,*
1
School of Materials Science and Engineering, University of Shanghai for Science and Technology, Shanghai 200093, China
2
Key Laboratory of Interfacial Physics and Technology, Shanghai Institute of Applied Physics, Chinese Academy of Sciences, Shanghai 201800, China
3
College of Materials Science and Engineering, Fuzhou University, Fuzhou, Fujian 350108, China
4
Dalian National Laboratory for Clean Energy, Dalian 116023, China
*
Authors to whom correspondence should be addressed.
†
Xiaodong Zuo and Zhiyi Chen contributed equally to this work.
Materials 2020, 13(10), 2267; https://doi.org/10.3390/ma13102267
Submission received: 14 April 2020 / Revised: 30 April 2020 / Accepted: 12 May 2020 / Published: 14 May 2020
Browse Figures
Versions Notes

Abstract

:
Nanoscale perovskite oxides with enhanced electrocatalytic activities have been widely used as oxygen electrodes of reversible solid oxide cells (RSOC). Here, La0.6Sr0.4FeO3−δ (LSF) nanoscale powder is synthesized via a novel molten salt method using chlorides as the reaction medium and fired at 850 °C for 5 h after removing the additives. A direct assembly method is employed to fabricate the LSF electrode without a pre-sintering process at high temperature. The microstructure characterization ensures that the direct assembly process will not damage the porosity of LSF. When operating as a solid oxide fuel cell (SOFC), the LSF cell exhibits a peak power density of 1.36, 1.07 and 0.7 W/cm2 at 800, 750 and 700 °C, respectively, while in solid oxide electrolysis cell (SOEC) mode, the electrolysis current density reaches 1.52, 0.98 and 0.53 A/cm2 under an electrolysis voltage of 1.3 V, respectively. Thus, it indicates that the molten salt routine is a promising method for the synthesis of highly active perovskite LSF powders for directly assembled oxygen electrodes of RSOC.

Graphical Abstract

1. Introduction

Reversible solid oxide cells (RSOC) are a novel energy conversion and storage device with the highest efficiency [1]. In solid oxide fuel cell (SOFC) mode, they can directly convert the chemical energy of clean fuels into electricity and heat [2], while in solid oxide electrolysis cell (SOEC) mode, they can convert electrical and thermal energy into chemical energy for storage [3]. The oxygen electrode, where the oxygen reduction reaction (ORR) and oxygen evolution reaction (OER) occur, is one of the dominant components that affect the overall performance and stability of the RSOC [4]. As a mixed electronic and ionic conductor (MIEC), (La,Sr)FeO3−δ (LSF) has been extensively studied to replace the conventional manganite based materials and exhibit much higher electrochemical performance at intermediate temperature (600–800 °C) [5,6]. LSF has a similar thermal expansion coefficient (TEC) to the zirconia-based electrolyte, as well as improved stability and lowered cost, compared to Sr-doped LaCoO3 material [7].
In general, decreasing the size of the electrode material grains will enlarge the specific surface and promote the electrochemical activities. For example, Fan et al. introduced nanosized La0.6Sr0.4FeO3−δ particles into YSZ scaffold via the infiltration method to fabricate nanostructured LSF/YSZ oxygen electrodes after firing at 850 °C for 5 h. The infiltrated cell exhibits a peak power density of 611 mW/cm2 using humidified H2 at 800 °C [8]. Another effective technology to fabricate perovskite electrocatalysts is the molten salt synthesis (MSS) method. Xue et al. have summarized some progress in the synthesis, characterization and potential applications of low-dimensional perovskite oxide nanostructures by the MSS method [9]. Song et al. obtained porous iron-rich La0.6Sr0.4Co0.2Fe0.8O2.9 (LSCF) at a lowered temperature of 850 °C, with enriched surface area and high activity [10]. Guan et al. employed the MSS method to synthesize Nb-doped LSF electrode for RSOC, achieving a peak power density of 0.79W/cm2 in SOFC mode and an electrolysis current density of 0.89A/cm2 in SOEC mode at 800 °C [11]. However, if the nanometric powders are for use as the oxygen electrode of RSOC, the negative effect of the conventional pre-sintering at the temperature of 1000–1200 °C on microstructural coarsening is not negligible [12]. High-temperature sintering accelerates Sr surface segregation (SSS) [13], which is the cause of formation of insulating SrZrO3 phases at the interface between the electrode and electrolyte. The SSS also leads to formation of SrCrO4 layers on the surface of the electrode [14,15]. Therefore, to mitigate the SSS phenomenon in the oxygen electrode, reducing the presintering temperature is favorable. An alternative strategy to lower the fabrication temperature is to use the direct assembly technique by applying a polarization current [16,17,18]. Ai et al. manufactured the LSCF electrode on barrier-layer-free yttria-stabilized zirconia (YSZ) electrolyte without presintering, achieving a current density of 1.5 A/cm2 at 750 °C and 1.26 V in 50% H2O/50% H2 [19]. The advantages of the directly assembled electrode also include the preservation of particle-shaped contact in the interface and the nanostructure of the particles [16], sharing the same effect of the infiltration process.
In this study, we use the MSS method to synthesize nanoscale La0.6Sr0.4FeO3−δ (LSF) material for the oxygen electrode of a directly assembled RSOC. Chloride salts are added in the reactants, forming a liquid environment to accelerate the reaction at a reduced temperature, and the added chlorides are removed by cleaning the resultant powders. The measurement results show that the directly assembled LSF electrode exhibits attractive electrochemical performance in both SOFC and SOEC modes.

2. Materials and Methods

2.1. Synthesis and Characterization of LSF Powders

The procedure of the MSS method used for the synthesis of LSF powders is shown in Figure 1a. La2O3 (99.9%, Aladdin, Shanghai, China), SrCO3 (99.9%, Alfa Aesar, Shanghai, China), Fe3O4 (99.9%, Adams Reagent Co Ltd., Shanghai, China), NaCl (99.9%, Aladdin) and KCl (99.9%, Aladdin) were used as the reactants and additives and mixed in an agate mortar by grinding. The weight ratio between the overall reactants and the salts was 1:5, while the molar ratio of NaCl and KCl was 1:1. The mixture was fired at 850 °C in air for 5 h. The chloride mixture can be liquidized at the firing temperature, leading to significantly enhanced motilities of the reactants, in contrast to the case of conventional solid-state reaction. After washing the resultant powder with deionized water using the centrifugal process, the obtained LSF powders were dried at 150 °C for 24 h, and the added salts could be recycled.
To confirm the phase evolution of as-synthesized and heat-treated LSF powders, X-ray diffraction (XRD) data were collected on a Bruker D8 Advance X-ray diffractometer (Karlsruhe, Baden-Württemberg, Germany) using the Ni-filtered Cu Kα radiation source at 40 kV and 40 mA (λ = 1.5148 Å), employing a scan rate of 1.5°/min in the 2θ range from 20 to 80°. Scanning electron microscopy (SEM) measurements were carried out using a Zeiss Merlin Compact LEO 1530 VP SEM (Jena, Thüringen, Germany). Transmission electron microscopy (TEM) characterization was carried out with FEI Tecnai G2 F20 electron microscopy (Hillsboro, OR, USA). X-ray photoelectron spectrometry (XPS) was utilized to evaluate the valence state of the elements in LSF with a Thermo Scientific ESCA-LAB 250Xi analyzer (Hillsboro, OR, USA), and the energy scale was internally calibrated by setting the C 1 s peak at 284.6 eV.

2.2. Fabrication and Measurement of the Button Cell with Directly Assembled LSF Electrode

A NiO (J.T. Baker, Avantor, Allentown, PA, USA)-YSZ (8 mol% Y2O3 stabilized zirconia, Tosoh, Shiba, Tokyo, Japan) hydrogen electrode-supported YSZ electrolyte film button cell was fabricated using slurry spin coating (VTC-100, MTI, Shenyang, Liaoning, China) and co-sintered at 1450 °C in air for 5 h. A Gd0.1Ce0.9O1.95 (GDC, AGC Seimi Chemical Co Ltd., Chigasaki, Kanagawa, Japan) interlayer was prepared on the YSZ film by slurry spin coating and sintered at 1250 °C in air for 2 h. LSF ink was prepared by mixing the porous LSF powders with an ink vehicle (VEH, Fuel Cell Materials) and screen-printed on the YSZ/GDC bilayer electrolyte films. The directly assembled LSF electrode was dried in an oven at 100 °C for 2 h without further pre-sintering process. The effective area of the oxygen electrode was 0.22 cm2.
The procedures of sealing and testing of the button cell in both SOFC mode and SOEC mode have been described in detail elsewhere [19]. Prior to the testing, the directly assembled LSF electrode was polarized at a constant current density of 0.5 A/cm2 and 750 °C under anodic mode to form the interface of the oxygen electrode and the electrolyte. Then, the measurement of the polarization performance and electrochemical impedance spectra (EIS) from 800 to 700 °C was carried out using a self-made testing system, composed of several gas mass flowmeters, a furnace and a Gamry Interface 1000E Potentiostat (Gamry Instruments, Warminster, PA, USA), as shown in Figure 1b. EIS data were collected in the frequency range of 100 k–0.01 Hz with an AC signal of 10 mV under open circuit conditions. The high-frequency intercept of EIS represents the ohmic resistance (RΩ) and the difference between low- and high-frequency intercepts is related to the electrode polarization resistance (Rp).

3. Results

3.1. Characterization of LSF Powders

The phase purity of the as-synthesized LSF powders was characterized by room temperature XRD. The crystallographic structure of all the powders, shown in Figure 2a, can be indexed with the orthorhombic perovskite phase belonging to the Pnma (62) space group (JCPDS no.37–1493). The unit cell lattice parameters were refined and calculated to be a = 5.553, b = 7.845 and c = 5.561 Å. The XRD patterns indicate that all the additive chlorides can be recycled. However, an extra shoulder peak next to the (121) reflection of LSF is observed, and it can be attributed to trace La-Sr-Fe solid solution. Figure 2b,c gives the SEM and TEM morphologies of LSF particles and reveals their porous structure. The particle size of LSF powders without ball-milling is between 100 and 300 nm, with lots of holes in the grains to form an obvious nanobowl-shaped structure. Additionally, the diameter of the holes is about 100 nm. The origin of the holes could be complex, including the corrosion of metals in the molten salt, the removal of the salt during the washing process, or the evaporation of gases and salts. However, there is no doubt that the porosity of the particles will enlarge the specific area and the number of active sites [10]. The EDS spectrum (Figure 2d) of the powders also confirms that all the additive chloride salts have been removed, and the overall XPS spectrum (Figure 2e) reveals the presence of elements of La, Sr, Fe and O. The core level spectrum of Fe 2p is displayed in Figure 2f and splits into two parts, Fe 2p3/2 and Fe 2p1/2. The main Fe 2p3/2 peak occurs at 710.7 eV, while the Fe 2p1/2 peak is observed at 724.0 eV. Based on the fitting and analysis of Fe 2p core level, Fe exists in mixed valence states of Fe2+ and Fe3+, and the relative molar ratio of Fe2+/Fe3+ is 1.12 [20,21,22,23]. As is reported, the lowered valence state of the transition metal Fe determines better oxygen ionic conductivity and catalytic activity of LSF, since the existing Fe2+ would induce the formation of oxygen vacancies [24,25].

3.2. Electrochemical Performance Measurement

3.2.1. SOFC Performance

Figure 3a shows the current–voltage–power curves of the button cell with directly assembled LSF oxygen electrode in SOFC mode, using H2 and air as fuel and oxidant. The initial maximum power densities (MPDs) are 1.36, 1.03 and 0.7 W/cm2 at 800, 750 and 700 °C, respectively. It is highlighted that the performance of the directly assembled LSF cell is comparable to presintered cells with cobalt-free electrodes, such as infiltrated La0.6Sr0.4FeO3−δ (611 mW/cm2 at 800 °C) and Nd2NiO4 (700 mW/cm2 at 700 °C), La0.8Sr0.2FeO3−δ prepared using the glycine-nitrate combustion method (950 mW/cm2 at 750 °C), as well as La0.6Sr0.4Fe0.9Nb0.1O3−δ (503 mW/cm2 at 700 °C), Sr2Fe1.5Mo0.5O6–δ (835 mW/cm2 at 900 °C), SrFe0.9Nb0.1O3−δ (407 mW/cm2 at 800 °C), Sm0.5Sr0.5Fe0.8Cu0.2O3−δ (808 mW/cm2 at 700 °C) and SrNb0.1Fe0.9O3−δ (919 mW/cm2 at 600 °C) [8,26,27,28,29,30,31,32]. We ascribe the excellent electrocatalytic activities of the directly assembled LSF electrode mainly to the enlarged porosity and high specific surface area, leading to more active sites.
The electrochemical impedance spectra under open circuit conditions as a function of temperature are shown in Figure 3b. The ohmic resistance RΩ is 0.128, 0.176 and 0.270 Ω·cm2 at 800, 750 and 700 °C, respectively. The polarization impedance Rp is 0.133, 0.177, 0.27 Ω·cm2 at the corresponding temperature. The calculated activation energy for the total polarization process of the directly assembled LSF cell is 0.726 eV (Figure 3c). To elucidate the contributions of elementary electrode processes, transformation to the distribution of relaxation times (DRT) analysis was applied. In Figure 3d, six peaks labelled as P1 to P6 can be identified clearly for each curve, and their peak areas reflect the relative polarization loss but cannot be quantified [33]. The impedance contributions have been discussed previously for a full solid oxide cell with six DRT signal peaks [34]. The high-frequency processes P1 (~16 kHz) and P2 (~1.8 kHz) are related to the oxygen ion transportation through the electrolyte or across the interfaces, while P3 (~600 Hz) is associated with the charge transferring in the electrodes. P4 (~15 Hz) relates to the diffusion and exchange of oxygen species at the three-phase boundaries (TPBs). The low-frequency processes P5 (0.1–1 Hz) and P6 (0.01–0.1 Hz) can be ascribed to the mass transfer of the reactants and gas conversion in the electrode. Obviously, as the temperature is elevated, significant decrease can be seen for process of P1, P2 and P3. However, the peak areas of the low-frequency processes (P4, P5, P6), dependent on the flux of the reactants, are not notably affected by the change of temperature. It is interesting that the summit frequencies of P5 and P6 decrease with increasing temperature, which can be ascribed to the enhanced mobility of gas molecules [33].

3.2.2. SOEC Performance

Figure 4a presents the temperature-dependent electrochemical performance of the button cell for CO2 electrolysis by feeding a mixture of H2 and CO2 to the hydrogen electrode. The electrolysis current densities are 1.52, 0.98 and 0.53 A/cm2 at 800, 750, 700 °C and 1.3 V. The performance is also as good as that of many other cobalt-free electrodes reported previously, such as infiltrated La0.6Sr0.4FeO3−δ (0.66 A/cm2 at 800 °C), La0.5Sr0.5Fe0.8Cu0.15Nb0.05O3−δ (0.85 A/cm2 at 800 °C), Sr2Fe1.5Mo0.5O6–δ (0.88 A/cm2 at 900 °C), La2NiO4+δ (0.39 A/cm2 at 800 °C), Nd2NiO4+δ (0.64 A/cm2 at 800 °C), La1.2Sr0.8NiO4 (1.37 A/cm2 at 700 °C) and Pr1.2Sr0.8NiO4 (1.12 A/cm2 at 700 °C) [8,35,36,37,38]. The EIS results are presented in Figure 4b. The ohmic resistance RΩ is 0.131, 0.145 and 0.185 Ω·cm2 at 800, 750 and 700 °C, respectively, while the polarization impedance Rp is 0.117, 0.222, 0.453 Ω·cm2 The calculated activation energy for the electrolysis process is 1.31 eV, higher than that in the fuel cell mode. In our opinion, after testing in SOFC mode, the sintering of the LSF electrode will affect the microstructure and increase the polarization impedance of the cell. Another possible reason for the higher activation energy could be related to the CO2 electrolysis reaction, for which the cell area-specific resistance value is even bigger than that of steam electrolysis [39]. The DRT analysis is also performed and shown in Figure 4d, proving that temperature has a great influence on the ion transportation and charge transfer resistance. For the directly assembled LSF cell, the insufficient oxygen ion conductivity of pure LSF might be one factor that results in the resistance. Therefore, the composite electrode, such as LSF-GDC, will yield lowered resistance. Another strategy is to develop novel mixed ionic–electronic conducting (MIEC) materials for intermediate temperature solid oxide cells.

3.3. Microstructure Analysis

Figure 5 shows the SEM image of the tested button cell with directly assembled LSF electrode after the anodic current polarization and electrochemical performance testing. We can see that the interface between the GDC interlayer and LSF oxygen electrode has been well induced in Figure 5a. Therefore, it provides evidence that the direct assembly method promises to decrease the contact resistance. In addition, most of the pores on LSF grains synthesized by the molten salt method have been well preserved, ensuring high electrochemical activities. However, the stability test for the porous particles needs to be carried out in the future. Additionally, according to the particle size distribution of LSF shown in Figure 5b, the size of most LSF particles is less than 400 nm, almost the same as the as-prepared powders. Thus, this indicates that the direct assembly method is also suitable for other nanoparticles or the materials easily decomposed at higher temperature to be used in electrodes of RSOC.

4. Discussion

Conventional hydrothermal and sol–gel methods can synthesize ultrafine nano powders, but it is difficult to realize mass production as easily as with the solid-state method. In comparison, the molten salt synthesis method, sharing many advantages of both the liquid-phase method and solid-state method, was utilized to produce nanometric LSF materials with special porous morphology (Figure 2b,c). As is reported, both the existence of iron and the molten salt approach play important roles in producing porous structures [10]. In a traditional RSOC oxygen electrode preparation process, high-temperature sintering limits the use of nanostructured materials. Therefore, the current polarization process, as effective as high-temperature presintering on the formation of the interface of electrode and electrolyte, was used to maintain the microstructure of the LSF electrode (Figure 5a), leading to the excellent performance of the button cell.
The key factor of the direct assembly method can be attributed to the Joule heat caused by the polarization current applied to the screen-printed electrode. Since the resistance of the electrolyte and the interface of the LSF electrode and GDC interlayer are larger than those of the electrodes, more Joule heat will be generated on the electrolyte and the interface. The phenomenon is consistent with resistance welding technology, which is commonly used in industry [40]. In practical application of the resistance welding technique, it is generally necessary to apply pressure to fix the components, and then the heat generated by the current passing through the contact of the weldment will be used for local heating welding. As for the directly assembled RSOC electrode, it has been fixed onto the electrolyte using a binder in the electrode ink. Thus, the welding effect on the interface of LSF electrode and GDC interlayer is mainly related to the applied polarization current and the contact resistance for the interface. Additionally, the contact of directly assembled electrodes might be improved owing to the high current polarization during the SOFC measurement. Since resistance welding technology has many advantages, such as being free of welding flux, high productivity, smaller deformation of weldment and ease of automation, we deduce that the direct assembly technology is also very promising in the fabrication of solid oxide cells.
In general, the combination of the MSS method and the direct assembly technique is proposed to provide solutions to the utilization of nanosized materials as electrode of solid oxide cells. In future, we will carry out detailed research on the relationship among the temperature, the polarization current, the interface contact resistance and the performance of direct assembly electrodes.

5. Conclusions

Porous LSF powders are prepared using a novel molten salt synthesis method as electrode materials of a reversible solid oxide cell. The direct assembly method is proposed to manufacture the LSF oxygen electrode to protect the nanostructure of the materials. Experimental results show that the directly assembled cell with porous LSF oxygen electrode reaches a maximum output power density of 1.36 W/cm2 at 800 °C in SOFC mode, while the electrolysis current density of the directly assembled cell is 1.52 A/cm2 at 1.3 V for CO2 electrolysis. The electrochemical testing results indicate that the combination of porous powders via the molten salt synthesis method and the directly assembled technology shows promise for the preparation of high-performance reversible solid oxide cells. Upcoming research will focus on durability and mechanism of the novel porous powders and directly assembled electrodes.

Author Contributions

X.Z. and Z.C. completed the experiments; C.G., S.S., G.X. and Y.P. discussed the results; X.Z. and C.G. wrote the manuscript; K.C. reviewed the manuscript; J.-Q.W. charged the project. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the “Transformational Technologies for Clean Energy and Demonstration”, Strategic Priority Research Program of the Chinese Academy of Sciences (XDA21000000), the Young Potential Program of Shanghai Institute of Applied Physics, Chinese Academy of Sciences (Y955111031) and the DNL Cooperation Fund, Chinese Academy of Sciences (DNL201923).

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Jensen, S.H.; Graves, C.; Mogensen, M.; Wendel, C.; Braun, R.; Hughes, G.; Gao, Z.; Barnett, S.A. Large-scale electricity storage utilizing reversible solid oxide cells combined with underground storage of CO2 and CH4. Energy Environ. Sci. 2015, 8, 2471–2479. [Google Scholar] [CrossRef]
  2. Minh, N.Q. Ceramic Fuel Cells. J. Am. Ceram. Soc. 1993, 76, 563–588. [Google Scholar] [CrossRef]
  3. Hansen, J.B. Solid oxide electrolysis—A key enabling technology for sustainable energy scenarios. Faraday Discuss. 2015, 182, 9–48. [Google Scholar] [CrossRef] [PubMed]
  4. Risch, M. Perovskite Electrocatalysts for the Oxygen Reduction Reaction in Alkaline Media. Catalysts 2017, 7, 154. [Google Scholar] [CrossRef] [Green Version]
  5. Simner, S.P.; Bonnett, J.F.; Canfield, N.L.; Meinhardt, K.D.; Shelton, J.P.; Sprenkle, V.L.; Stevenson, J.W. Development of lanthanum ferrite SOFC cathodes. J. Power Sources 2003, 113, 1–10. [Google Scholar] [CrossRef]
  6. Kim, M.C.; Park, S.J.; Haneda, H.; Tanaka, J.; Shirasaki, S. High temperature electrical conductivity of La1−xSrxFeO3−δ (x > 0.5). Solid State Ionics 1990, 40, 239–243. [Google Scholar]
  7. Wu, T.; Yu, B.; Zhang, W.; Chen, J.; Zhao, S. Fabrication of a high-performance nano-structured Ln1−xSrxMO3−δ (Ln=La, Sm; M=Mn, Co, Fe) SOC electrode through infiltration. RSC Adv. 2016, 6, 68379–68387. [Google Scholar] [CrossRef]
  8. Fan, H.; Zhang, Y.; Han, M. Infiltration of La0.6Sr0.4FeO3-δ nanoparticles into YSZ scaffold for solid oxide fuel cell and solid oxide electrolysis cell. J. Alloys Compd. 2017, 723, 620–626. [Google Scholar] [CrossRef]
  9. Xue, P.; Wu, H.; Lu, Y.; Zhu, X. Recent progress in molten salt synthesis of low-dimensional perovskite oxide nanostructures, structural characterization, properties, and functional applications: A review. J. Mater. Sci. Technol. 2018, 34, 914–930. [Google Scholar] [CrossRef]
  10. Song, S.; Zhou, J.; Zhang, S.; Zhang, L.; Li, J.; Wang, Y.; Han, L.; Long, Y.; Hu, Z.; Wang, J.-Q. Molten-salt synthesis of porous La0.6Sr0.4Co0.2Fe0.8O2.9 perovskite as an efficient electrocatalyst for oxygen evolution. Nano Res. 2018, 11, 4796–4805. [Google Scholar] [CrossRef]
  11. Guan, C.; Wang, Y.; Chen, K.; Xiao, G.; Lin, X.; Zhou, J.; Song, S.; Wang, J.-Q.; Zhu, Z.; Zhou, X.-D. Molten salt synthesis of Nb-doped (La, Sr)FeO3 as the oxygen electrode for reversible solid oxide cells. Mater. Lett. 2019, 245, 114–117. [Google Scholar] [CrossRef]
  12. Hardy, J.S.; Templeton, J.W.; Edwards, D.J.; Lu, Z.; Stevenson, J.W. Lattice expansion of LSCF-6428 cathodes measured by in situ XRD during SOFC operation. J. Power Sources 2012, 198, 76–82. [Google Scholar] [CrossRef]
  13. Caillol, N.; Pijolat, M.; Siebert, E. Investigation of chemisorbed oxygen, surface segregation and effect of post-treatments on La0.8Sr0.2MnO3 powder and screen-printed layers for solid oxide fuel cell cathodes. Appl. Surf. Sci. 2007, 253, 4641–4648. [Google Scholar] [CrossRef]
  14. Kindermann, L.; Das, D.; Nickel, H.; Hilpert, K. Chemical compatibility of the LaFeO3 base perovskites (La0.6Sr0.4)(z)Fe(0.8)M(0.2)O(3-delta) (z=1, 0.9; M=Cr, Mn, Co, Ni) with yttria stabilized zirconia. Solid State Ionics 1996, 89, 215–220. [Google Scholar] [CrossRef]
  15. Ardigò, M.R.; Perron, A.; Combemale, L.; Heintz, O.; Caboche, G.; Chevalier, S. Interface reactivity study between La0.6Sr0.4Co0.2Fe0.8O3−δ (LSCF) cathode material and metallic interconnect for fuel cell. J. Power Sources 2011, 196, 2037–2045. [Google Scholar] [CrossRef]
  16. Jiang, S.P. Thermally and Electrochemically Induced Electrode/Electrolyte Interfaces in Solid Oxide Fuel Cells: An AFM and EIS Study. J. Electrochem. Soc. 2015, 162, F1119–F1128. [Google Scholar] [CrossRef] [Green Version]
  17. Li, N.; Ai, N.; Chen, K.; Cheng, Y.; He, S.; Saunders, M.; Dodd, A.; Suvorova, A.; Jiang, S.P. In situ assembled La0.8Sr0.2MnO3 cathodes on a Y2O3–ZrO2 electrolyte of solid oxide fuel cells-interface and electrochemical activity. RSC Adv. 2016, 6, 99211–99219. [Google Scholar] [CrossRef]
  18. Chen, K.; Li, N.; Ai, N.; Cheng, Y.; Rickard, W.D.A.; Jiang, S.P. Polarization-Induced Interface and Sr Segregation of in Situ Assembled La0.6Sr0.4Co0.2Fe0.8O3−δ Electrodes on Y2O3-ZrO2 Electrolyte of Solid Oxide Fuel Cells. ACS Appl. Mater. Interfaces 2016, 8, 31729–31737. [Google Scholar] [CrossRef]
  19. Ai, N.; He, S.; Li, N.; Zhang, Q.; Rickard, W.D.A.; Chen, K.; Zhang, T.; Jiang, S.P. Suppressed Sr segregation and performance of directly assembled La0.6Sr0.4Co0.2Fe0.8O3−δ oxygen electrode on Y2O3-ZrO2 electrolyte of solid oxide electrolysis cells. J. Power Sources 2018, 384, 125–135. [Google Scholar] [CrossRef]
  20. Graat, P.C.J.; Somers, M.A.J. Simultaneous determination of composition and thickness of thin iron-oxide films from XPS Fe 2p spectra. Appl. Surf. Sci. 1996, 100, 36–40. [Google Scholar] [CrossRef]
  21. Seyama, H.; Soma, M. Bonding-state characterization of the constituent elements of silicate minerals by X-ray photoelectron spectroscopy. J. Chem. Soc. Faraday Trans. 1985, 81, 485–495. [Google Scholar] [CrossRef]
  22. Allen, G.C.; Curtis, M.T.; Hooper, A.J. X-Ray photoelectron spectroscopy of iron-oxygen systems. J. Chem. Soc. Dalton Trans. 1974, 14, 1525–1530. [Google Scholar] [CrossRef]
  23. Langevoort, J.C.; Sutherland, I.; Hanekamp, L.J.; Gellings, P.J. On the oxide formation on stainless steels AISI 304 and incoloy 800H investigated with XPS. Appl. Surf. Sci. 1987, 28, 167–179. [Google Scholar] [CrossRef] [Green Version]
  24. Li, J.; Wei, B.; Cao, Z.; Yue, X.; Zhang, Y.; Lü, Z. Niobium doped lanthanum strontium ferrite as a redox-stable and sulfur-tolerant anode for solid oxide fuel cells. ChemSusChem 2018, 11, 254–263. [Google Scholar] [CrossRef]
  25. Nitadori, T.; Misono, M. Catalytic properties of La1−xA′xFeO3(A′=Sr, Ce) and La1−xCexCoO3. J. Catal. 1985, 93, 459–466. [Google Scholar] [CrossRef]
  26. LagunaBercero, M.; Hanifi, A.; Monzon, H.; Cunningham, J.; Etsell, T.H.; Sarkar, P. High performance of microtubular solid oxide fuel cells using Nd2NiO4+δ-based composite cathodes. J. Mater. Chem. A 2014, 2, 9764–9770. [Google Scholar] [CrossRef] [Green Version]
  27. Simner, S.P.; Bonnett, J.F.; Canfield, N.L.; Meinhardt, K.D.; Sprenkle, V.L.; Stevenson, J.W. Optimized Lanthanum Ferrite-Based Cathodes for Anode-Supported SOFCs. Electrochem. Solid State Lett. 2002, 5, A173–A175. [Google Scholar] [CrossRef]
  28. Yu, T.; Mao, X.; Ma, G. Performance of cobalt-free perovskite La0.6Sr0.4Fe1−xNbxO3−δ cathode materials for proton-conducting IT-SOFC. J. Alloys Compd. 2014, 608, 30–34. [Google Scholar] [CrossRef]
  29. Liu, Q.; Dong, X.; Xiao, G.; Zhao, F.; Chen, F. A Novel Electrode Material for Symmetrical SOFCs. Adv. Mater. 2010, 22, 5478–5482. [Google Scholar] [CrossRef]
  30. Zhou, Q.; Zhang, L.; He, T. Cobalt-free cathode material SrFe0.9Nb0.1O3−δ for intermediate-temperature solid oxide fuel cells. Electrochem. Commun. 2010, 12, 285–287. [Google Scholar] [CrossRef]
  31. Ling, Y.; Zhao, L.; Lin, B.; Dong, Y.; Zhang, X.; Meng, G.; Liu, X. Investigation of cobalt-free cathode material Sm0.5Sr0.5Fe0.8Cu0.2O3−δ for intermediate temperature solid oxide fuel cell. Int. J. Hydrogen Energy 2010, 35, 6905–6910. [Google Scholar] [CrossRef]
  32. Jiang, S.; Liang, F.; Zhou, W.; Shao, Z. Hierarchical porous cobalt-free perovskite electrode for highly efficient oxygen reduction. J. Mater. Chem. 2012, 22, 16214–16218. [Google Scholar] [CrossRef]
  33. Sun, X.; Bonaccorso, A.D.; Graves, C.; Ebbesen, S.D.; Jensen, S.H.; Hagen, A.; Holtappels, P.; Hendriksen, P.V.; Mogensen, M.B. Performance Characterization of Solid Oxide Cells Under High Pressure. Fuel Cells 2015, 15, 697–702. [Google Scholar] [CrossRef]
  34. Zhou, Y.; Zhou, Z.; Song, Y.; Zhang, X.; Guan, F.; Lv, H.; Liu, Q.; Miao, S.; Wang, G.; Bao, X. Enhancing CO2 electrolysis performance with vanadium-doped perovskite cathode in solid oxide electrolysis cell. Nano Energy 2018, 50, 43–51. [Google Scholar] [CrossRef]
  35. Zhou, N.; Yin, Y.-M.; Li, J.; Xu, L.; Ma, Z.-F. A robust high-performance cobalt-free oxygen electrode La0.5Sr0.5Fe0.8Cu0.15Nb0.05O3−δ for reversible solid oxide electrochemical cell. J. Power Sources 2017, 340, 373–379. [Google Scholar] [CrossRef]
  36. Liu, Q.; Yang, C.; Dong, X.; Chen, F. Perovskite Sr2Fe1.5Mo0.5O6−δ as electrode materials for symmetrical solid oxide electrolysis cells. Int. J. Hydrogen Energy 2010, 35, 10039–10044. [Google Scholar] [CrossRef]
  37. Chauveau, F.; Mougin, J.; Mauvy, F.; Bassat, J.-M.; Grenier, J.-C. Development and operation of alternative oxygen electrode materials for hydrogen production by high temperature steam electrolysis. Int. J. Hydrogen Energy 2011, 36, 7785–7790. [Google Scholar] [CrossRef]
  38. Yang, S.; Wen, Y.; Zhang, J.; Lu, Y.; Ye, X.; Wen, Z. Electrochemical performance and stability of cobalt-free Ln1.2Sr0.8NiO4(Ln=La and Pr) air electrodes for proton-conducting reversible solid oxide cells. Electrochim. Acta 2018, 267, 269–277. [Google Scholar] [CrossRef]
  39. Stoots, C.M.; O’Brien, J.E.; Herring, J.S.; Hartvigsen, J.J. Syngas production via high-temperature coelectrolysis of steam and carbon dioxide. J. Fuel. Cell Sci. Technol. 2009, 6, 011014. [Google Scholar] [CrossRef]
  40. Vignesh, K.; Perumal, A.E.; Velmurugan, P. Optimization of resistance spot welding process parameters and microstructural examination for dissimilar welding of AISI 316L austenitic stainless steel and 2205 duplex stainless steel. Int. J. Adv. Manuf. Technol. 2017, 93, 455–465. [Google Scholar] [CrossRef]
Materials 13 02267 g001 550
Figure 1. Schematic diagrams of molten salt synthesis procedures of La0.6Sr0.4FeO3−δ (LSF) powders (a) and the button cell test apparatus (b).
Figure 1. Schematic diagrams of molten salt synthesis procedures of La0.6Sr0.4FeO3−δ (LSF) powders (a) and the button cell test apparatus (b).
Materials 13 02267 g001
Materials 13 02267 g002 550
Figure 2. (a) XRD patterns of LSF powders; (b) SEM, (c) TEM images and (d) EDS spectrum of the particles; (e) overall XPS spectrum and (f) Fe 2p core level of LSF.
Figure 2. (a) XRD patterns of LSF powders; (b) SEM, (c) TEM images and (d) EDS spectrum of the particles; (e) overall XPS spectrum and (f) Fe 2p core level of LSF.
Materials 13 02267 g002
Materials 13 02267 g003 550
Figure 3. (a) I–V discharge curves, (b) the impedance spectra, (c) the activation energy for the polarization process and (d) the distribution of relaxation times (DRT) analysis of the impedance spectra of the directly assembled LSF cell in solid oxide fuel cell (SOFC) mode at 700–800 °C.
Figure 3. (a) I–V discharge curves, (b) the impedance spectra, (c) the activation energy for the polarization process and (d) the distribution of relaxation times (DRT) analysis of the impedance spectra of the directly assembled LSF cell in solid oxide fuel cell (SOFC) mode at 700–800 °C.
Materials 13 02267 g003
Materials 13 02267 g004 550
Figure 4. (a) I–V charge curves, (b) the impedance spectra, (c) the activation energy for the polarization process and (d) the DRT analysis of the impedance spectra for CO2 electrolysis at 700–800 °C.
Figure 4. (a) I–V charge curves, (b) the impedance spectra, (c) the activation energy for the polarization process and (d) the DRT analysis of the impedance spectra for CO2 electrolysis at 700–800 °C.
Materials 13 02267 g004
Materials 13 02267 g005 550
Figure 5. Interface of yttria-stabilized zirconia (YSZ) electrolyte/ Gd0.1Ce0.9O1.95 (GDC) interlayer/LSF oxygen electrode in the directly assembled button cell (a) and the particle size distribution of LSF grains (b).
Figure 5. Interface of yttria-stabilized zirconia (YSZ) electrolyte/ Gd0.1Ce0.9O1.95 (GDC) interlayer/LSF oxygen electrode in the directly assembled button cell (a) and the particle size distribution of LSF grains (b).
Materials 13 02267 g005

Share and Cite

MDPI and ACS Style

Zuo, X.; Chen, Z.; Guan, C.; Chen, K.; Song, S.; Xiao, G.; Pang, Y.; Wang, J.-Q. Molten Salt Synthesis of High-Performance, Nanostructured La0.6Sr0.4FeO3−δ Oxygen Electrode of a Reversible Solid Oxide Cell. Materials 2020, 13, 2267. https://doi.org/10.3390/ma13102267

AMA Style

Zuo X, Chen Z, Guan C, Chen K, Song S, Xiao G, Pang Y, Wang J-Q. Molten Salt Synthesis of High-Performance, Nanostructured La0.6Sr0.4FeO3−δ Oxygen Electrode of a Reversible Solid Oxide Cell. Materials. 2020; 13(10):2267. https://doi.org/10.3390/ma13102267

Chicago/Turabian Style

Zuo, Xiaodong, Zhiyi Chen, Chengzhi Guan, Kongfa Chen, Sanzhao Song, Guoping Xiao, Yuepeng Pang, and Jian-Qiang Wang. 2020. "Molten Salt Synthesis of High-Performance, Nanostructured La0.6Sr0.4FeO3−δ Oxygen Electrode of a Reversible Solid Oxide Cell" Materials 13, no. 10: 2267. https://doi.org/10.3390/ma13102267

APA Style

Zuo, X., Chen, Z., Guan, C., Chen, K., Song, S., Xiao, G., Pang, Y., & Wang, J. -Q. (2020). Molten Salt Synthesis of High-Performance, Nanostructured La0.6Sr0.4FeO3−δ Oxygen Electrode of a Reversible Solid Oxide Cell. Materials, 13(10), 2267. https://doi.org/10.3390/ma13102267

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop