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. 2019 Dec 4;4(25):21494–21499. doi: 10.1021/acsomega.9b03193

In Situ Exsolved Ni-Decorated Ba(Ce0.9Y0.1)0.8Ni0.2O3−δ Perovskite as Carbon-Resistant Composite Anode for Hydrocarbon-Fueled Solid Oxide Fuel Cells

Yanya Liu †, Lichao Jia †,‡, Bo Chi †,‡,*, Jian Pu †,‡, Jian Li †,‡
PMCID: PMC6921628  PMID: 31867545

Abstract

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In this study, in situ exsolved Ni–Ba(Ce0.9Y0.1)0.8Ni0.2O3−δ+Gd0.1Ce0.9O1.9 (Ni–BCYN+GDC) perovskite anode is studied for application in hydrocarbon-fueled solid oxide fuel cell (SOFC). The electrocatalytic activities of the oxidation reaction of anode in hydrogen and methane atmospheres are studied. The results show that the surface-exsolved Ni nanoparticles can significantly improve the electrochemical properties of the anode. The polarization resistances of the studied anode in hydrogen and methane atmospheres at 750 °C are as low as 0.0042 and 0.0054 Ω·cm–2, respectively. At the same time, a 36 h short-term open-circuit voltage test under a methane atmosphere confirms that the Ni–BCYN+GDC composite anode exhibits a good carbon deposition resistance. These results demonstrate that the Ni–BCYN+GDC composite anode is a potential novel anode material candidate for hydrocarbon-fueled SOFC.

1. Introduction

Solid oxide fuel cell (SOFC) can convert fuels’ chemical energy into electricity with high efficiencies.1 SOFC has the advantage of fuel flexibility with wide fuel options and can use hydrocarbons as fuel,2 and hydrocarbon fuels are much cheaper and easier to be prepared, transported, and stored than hydrogen fuel. The conventional anode material for SOFC is Ni-based cermet.3 The Ni-based anodes4 have a high electrocatalytic activity for H2 oxidation. However, Ni is prone to forming carbon filaments by a mechanism that involves carbon deposition,5,6 dissolution into the Ni particles,7 precipitation at the interface between the Ni particles and the substrate,8,9 and uplifting the Ni particles from the substrate.10,11 Therefore, novel alternative carbon-tolerant anode materials are highly expected. Researchers have begun to study Ni-free metal oxide based materials,12 such as La0.6Sr0.4Co0.2Fe0.8O3−δ,13 La0.75Sr0.25Cr0.5Mn0.5O3−δ,14 La0.7Sr0.3Cr0.8Ti0.2O3−δ,15 and BaZr0.1Ce0.7Y0.1Yb0.1O3−δ.16 Although these materials have a better carbon tolerance, their electrochemical performance and stability when using hydrocarbon fuels are not comparable to those of Ni-based cermets.17 Then, improvements in these anode materials have been attempted to enhance the electrochemical performance18 through nanoparticle decoration.19,20 Apart from improving Ni-based cermet anodes, the modifications may improve their carbon deposition resistance by impregnating nanoparticles on Ni-based anodes. Li et al.21 studied the Ni–GDC anode with impregnated BaCe0.9Yb0.1O3−δ (BCYb) nanoparticles and found excellent carbon deposition resistance performance in methane. The in situ exsolution of metal nanoparticles on ceramic anode has also been investigated with enhanced electrochemical performance, such as Ni–Sr0.95(Ti0.3Fe0.63Ni0.07)O3−δ-,22 FeNi3–Sr2FeMo0.65Ni0.35O6−δ-,23 and Ni–Ba(Zr0.4Ce0.4Y0.2)0.8Ni0.2O3−δ (BZCYN)-infiltrated Sm0.2Ce0.8O1.9 (SDC) anode.24 In situ exsolution can obtain ceramic anode with a uniform distribution of metal nanoparticles and a larger reaction three-phase interfaces;25 this anode has excellent electrochemical performance.

BaCe0.9Y0.1 (BCY) has good oxygen ion and proton conductivity, which is determined by the operating temperature and working atmosphere.26 It has been reported in the literature that the proton conductivity of BCY is beneficial to the oxidation of hydrocarbon fuels.21 In this study, BCY is selected as the base perovskite phase to enhance the chemical stability and carbon deposition resistance of anode. Doping Ni into the B sites of the perovskite lattice of BCY can obtain Ba(Ce0.9Y0.1)0.8Ni0.2O3−δ (BCYN), which has better electrocatalytic activity for hydrocarbon oxidation; then, Ni is in situ exsolved on BCYN by reduction. The exsolved Ni nanoparticles are in close contact with the matrix BCYN with evenly distribution, which can improve the catalytic performance of the anode and alleviate the formation of carbon deposition.

2. Results and Discussion

2.1. Phase Structure

The phase composition of the calcined BCY and BCYN powders were characterized by X-ray diffraction (XRD), as shown in Figure 1a. The XRD peaks of BCYN are consistent with the ICDD file for BaCe0.9Y0.1, confirming the purity of BCY phase without impure phase after calcination, which proves that Ni is doped into the perovskite lattice of BCY. However, after BCYN was reduced in 5% H2–N2 atmosphere for 8 h, the diffraction peaks of Ni appear, accompanied by those of BCY phase, which can prove that Ni is exsolved from BCYN. The BCYN and GDC powders were co-calcined at 1000 °C and tested by XRD. The test results are shown in Figure 1b. The result shows that no heterogeneous phase other than BCYN and GDC appears, and both BCYN and GDC are normal phases, indicating that these two materials are chemically compatible.

Figure 1.

Figure 1

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XRD patterns of (a) BCYN and Ni–BCYN powders reduced in 5% H2–N2 for 8 h and (b) BCYN+GDC co-calcined in air atmosphere at 1000 °C for 2 h.

2.2. Microstructure Characterization

Figure 2a is the cross-sectional view of a symmetric cell supported by a GDC electrolyte. The GDC electrolyte is densely sintered and in good contact with the electrodes, with the thickness of about 230 μm. Figure 2b shows that the BCYN+GDC anode has the thickness of ∼36 μm with well adherence to the electrolyte. Before working in the reducing atmosphere, the BCYN+GDC anode grains show a smooth surface. At the same time, the close connection between the grains forms a porous anode structure (Figure 2c). For the reduced anode, many isolated nanoparticles appear on smooth grains and grain boundaries (Figure 2d), which is related to the exsolved Ni nanoparticles.

Figure 2.

Figure 2

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Scanning electron microscopy (SEM) morphologies of (a) GDC electrolyte-based symmetric cell and (b) the BCYN+GDC anode; top-view of the BCYN+GDC anode (c) before and (d) after reduction.

The electron probe microanalyzer (EPMA) test was conducted to further investigate the distribution of Ni nanoparticles on the anode. It can be seen from the EPMA result in Figure 3 that Ni is homogeneously dispersed on the anode, and there is no O element around Ni element, so it can be concluded that Ni exists as a simple substance, which combines the evidence of the XRD patterns.

Figure 3.

Figure 3

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EPMA elemental mapping within the anode surface.

2.3. Symmetric Cell Performance in H2 and CH4

Figure 4 shows the electrochemical impedance spectra (EIS) of Ni–BCYN+GDC symmetric cells in wet H2 (with 3% H2O) and CH4 (with 3% H2O), measured under open-circuit voltage (OCV) condition at 600–750 °C. The entire symmetric cell was placed in 5% H2–N2 reducing atmosphere for 8 h before testing.

Figure 4.

Figure 4

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EIS results of cell with Ni–BCYN+GDC anode under (a) wet H2 and (b) wet CH4 at 600–750 °C.

The high-frequency intercept of the impedance spectra represents the ohmic resistance (RΩ), which mainly reflects the performance of the electrolyte. Polarization impedance (RP) is the difference between low-frequency and high-frequency resistances, which mainly reflects the performance related to the electrode processes. Due to the electrochemical behavior of thermal activation, all the impedances of the cell decrease with increasing temperature. Figure 4a shows RΩ for the reaction in wet H2, which is 1.05, 0.71, 0.54, and 0.34 Ω·cm–2 at 600–750 °C, respectively. The corresponding RP value in wet H2 is 0.034, 0.01, 0.0054, and 0.0042 Ω·cm–2, respectively. The polarization impedance results are much smaller than those in the references. Li et al.27 studied M-BZCYYb anode and found the most excellent anode RP in H2 at 750 °C was about 0.064 Ω·cm–2. Song et al.24 studied the BZCYN-infiltrated SDC anode and found that the polarization impedance in H2 at 800 °C was 0.015 Ω·cm–2.

Figure 4b is the impedances of Ni–BCYN+GDC anode in a wet CH4 atmosphere. The results are listed in Table 1. The values of RP for the anode in wet CH4 are only about 0.055, 0.018, 0.008, and 0.0054 Ω·cm–2 at 600–750 °C, respectively. Compared with those of the anode working in a wet H2, RΩ and RP of the symmetric cells are basically the same order of magnitude in two different atmospheres, and RP obtained in the two fuels is extremely small. It can be inferred that the anode has excellent oxidation performance in methane.

Table 1. EIS Results of Cell with Ni–BCYN+GDC Anode under Wet H2 and Wet CH4 at Different Temperatures.

  temperature (°C) 750 700 650 600
H2 RΩ (Ω·cm–2) 0.50 0.57 0.67 0.96
  RP (Ω·cm–2) 0.0042 0.0054 0.01 0.034
CH4 RΩ (Ω·cm–2) 0.34 0.54 0.71 1.05
  RP (Ω·cm–2) 0.0054 0.008 0.018 0.055
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It can be presumed that the Ni nanoparticles on the anode can greatly increase the active site reactive. Since the precipitated particles are nanosized with a large specific surface area, more fuel gases can be contacted per unit area, thereby greatly improving the catalytic activity.

2.4. Full Cell Performance in H2 and CH4

Figure 5a shows the open-circuit EIS of H2 (with 3% H2O) oxidation reaction on anode before and after reduction at 750 °C, where the reduced curve is enlarged to an inset figure. It can be found that RΩ decreases dramatically due to the metal Ni particles exsolution on the anode after reduction.27 The corresponding RΩ is 3.22 Ω·cm–2 before reduction but decreases to 1.02 Ω·cm–2 after reduction. The ohmic impedance is drastically reduced because of the exsolution of Ni particles. Also, the values of RP are 0.25 and 1.50 Ω·cm–2 before and after reduction, respectively. The performance improvement can be attributed to the Ni nanoparticles exsolved from the Ni–BCYN+GDC anode matrix. The presence of the Ni nanoparticles not only increases the catalytic activity but also increases the reactive sites, so that RP of the cell can be significantly reduced, and the electrochemical performance is remarkably improved. The impedance results fitted by the equivalent circuit R(R1Q1)(R2Q2) are listed in Table 2.

Figure 5.

Figure 5

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(a) EIS of the cell with BCYN+GDC anode before and after reduction at 750 °C in H2; (b) EIS of the cell with BCYN+GDC anode before and after reduction at 700 and 750 °C in wet CH4; (c) I–V curve of the cell with the anode before and after reduction at 750 °C in wet H2; (d) I–V curve of the cell before and after reduction at 700 and 750 °C in wet CH4.

Table 2. EIS Results of BCYN+GDC and Ni–BCYN+GDC Anode in Wet H2 and CH4.

  H2
 CH4
anode temperature (°C) R (Ω·cm–2) R1 (Ω·cm–2) R2 (Ω·cm–2) temperature (°C) R (Ω·cm–2) R1 (Ω·cm–2) R2 (Ω·cm–2)
BCYN+GDC 750 3.22 0.68 0.82 750 4.15 1.56 2.46
700 4.17 1.62 4.16
Ni–BCYN+GDC 750 1.025 0.05 0.20 750 1.18 0.12 0.18
700 1.928 0.84 0.58
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Figure 5b shows EIS of the cell with BCYN+GDC anode measured in CH4 (with 3% H2O), where the reduced curve at 750 °C is enlarged to an inset figure. The figure shows similar results as the cell measured in H2 (with 3% H2O). The value of RP of the cell is 4.02 Ω·cm–2 at 750 °C before reduction but decreases sharply to 0.3 Ω·cm–2 after reduction. There is also a remarkable decrease of RΩ from 4.15 to 1.18 Ω·cm–2 for the cell before and after reduction.

Figure 5c is the I–V curve of the cell with Ni–BCYN+GDC anode measured in wet H2. Also, the OCV is around 0.78 V. The low OCV of GDC is due to the electronic conductivity of GDC electrolyte at high temperature.28 The maximum power density is about 22 and 91 mW·cm–2 at 750 °C before and after reduction, respectively. It can be found that the output can increase more than 4 times after Ni nanoparticle exsolution, which is consistent with the apparent decrease of RP after anode reduction.

Figure 5d is the I–V curve of the cell with Ni–BCYN+GDC anode measured in wet CH4 (with 3% H2O) at 700 and 750 °C. It shows that the anode can improve the polarization performance significantly. For cell with reduced anode, the maximum power density is 80 mW·cm–2 at 750 °C, which is higher than the cell with an unreduced anode. Similar change can also be observed at 700 °C.

Nagamori et al.28 found that decrease in the GDC electrolyte thickness from 600 to 30 μm could increase its power density nearly 3 times. In this work, to ensure the reliability of the operation, the electrolyte thickness is ∼540 μm. Formally, due to such a thick electrolyte, the ohmic impedance is extremely large, affecting the output performance. The thinner the electrolyte layer, the better the cell performance that can be obtained. At the same time, it is speculated that although the catalytic activity of the nanoparticles on the fuel gas is very high, the conductivity of the anode is insufficient due to the insufficient amount of exsolved Ni particles, the network conduction system is not formed, and the electrons cannot be efficiently transported, resulting in low peak power density.

2.5. Carbon Resistance of the Cell in Wet CH4

The carbon resistance of the Ni–BCYN+GDC anode was further studied in wet CH4 (with 3% H2O) at 750 °C under OCV. Compared with condition under the applied current, the anode under OCV is more likely to deposit carbon because the oxygen ions from the cathode under OCV cannot oxidize the carbon deposited on the anode, nor can it generate carbon-resistant water on the anode surface.29

It can be found that OCV gradually decreases from 0.81 to 0.74 V at the initial test period and tends to become stable around 0.78 V for 36 h (Figure 6a), consistent with the reported OCV trend with methane fuel.23,30 OCV is related to the volumetric partial pressure of the anode surface gas.31 Methane is not directly combined with oxygen ions; instead, it is catalytically decomposed before the working electrode participating in the reaction and is mainly decomposed into H2 and partially converted into CO. Since the methane fuel is not fully catalytically decomposed, the partial pressure of H2 on the anode surface decreases, resulting in the decrease of OCV and performance, which is consistent with the previously measured I–V curve.

Figure 6.

Figure 6

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(a) Stability of cell with Ni–BCYN+GDC anode in wet CH4 under OCV at 750 °C for 36 h. (b) Raman spectra and (c) SEM micrograph of the anode after short-term test in wet CH4 at 750 °C for 36 h under OCV.

SEM morphology analysis and Raman spectroscopy test were conducted about the cell after 36 h of short-term testing. The results are shown in Figure 6. In Raman spectra (Figure 6b), it can be seen that the peaks at 1350 and 1580 cm–1 associated with graphite are absent. Figure 6c shows the micrograph of the anode after being tested in wet CH4 for 36 h and that no carbon fibers can be found on the surface. These results confirm that Ni in situ exsolved BCYN+GDC anode is stable during 36 h test without carbon deposition.

3. Conclusions

In situ exsolved Ni-decorated Ba(Ce0.9Y0.1)0.8Ni0.2O3−δ perovskite is studied as a composite anode for hydrocarbon-fueled SOFC. In the oxidation reaction of hydrogen and methane at 750 °C, the anode exhibits excellent electrochemical activity. The polarization resistances of the anode in a symmetrical cell are 0.0042 and 0.0054 Ω·cm–2 in wet H2 and wet CH4, respectively. The composite anode also exhibits good resistant to carbon deposition even under OCV test environment where carbon deposition is more likely to occur in short term. The research work verifies that in situ exsolved Ni–BCYN+GDC composite anode is a potential novel anode candidate with good carbon resistance and electrochemical properties for hydrocarbon-fueled SOFC.

4. Experimental Section

BCYN powders with the composition of Ba(Ce0.9Y0.1)0.8Ni0.2O3−δ were prepared by the sol–gel process. All raw materials were from Sinopharm, Shanghai. Ba(NO3)2, Ce(NO3)3·6H2O, Y(NO3)3·6H2O, and Ni(NO3)2·6H2O are used as starting materials. All compounds are first dissolved in deionized water and then ethylenediaminetetraacetic acid (EDTA) complexing agent is added to form a gel. Then, the as-prepared gel is dried and calcined at 1000 °C for 3 h to obtain BCYN powders. The BaCe0.9Y0.1 (BCY) powders as a reference were also prepared in the same manner. Then, BCYN powders were reduced in 5% H2–N2 at 750 °C for 8 h to study the exsolution properties of the compounds. BCYN and Gd0.1Ce0.9O1.9 (GDC) powders were mixed in a weight ratio of 1:1 and calcined at 1000 °C for 2 h to determine their chemical compatibility by XRD test. To prepare the composite anode, BCYN and GDC powders were mixed at a weight ratio of 6:4 using ball milling in ethanol. The cathode used is composed of La0.6Sr0.4Co0.2Fe0.8O3−δ (LSCF) and GDC. The preparation process can be referred to in our previous works.32

The GDC electrolyte supported symmetric cells and full cells (Φ12 mm × 1 mm) were made by the molding and sintering process. The GDC powders were ball-milled in ethanol and then molded into a pellet and sintered at 1550 °C for 5 h. The area of the BCYN+GDC anode is 0.5 cm2 for symmetric cells. For the symmetric cells, the BCYN and GDC mixing slurry was screen-printed on the both sides of the mechanically polished electrolyte and sintered at 1000 °C in air for 2 h. For the full cell preparation, the same process was used to print the anode only on one side of the electrolyte, while LSCF+GDC composite cathode was prepared by slurry painting using 70 wt % LSCF and 30 wt % GDC, followed by sintering at 1000 °C for 2 h. The active areas of both full cells are 0.2 cm2.

Pt paste (Sino-Platinum Metals Co.) was painted on the anode and cathode for current collection for electrochemical measurement. A glass sealant (Ceramabond, Aremco Product Inc.) was used to seal the cells onto an Al2O3 tube. A 5% H2–N2 mixing gas was used to reduce the anodes in situ at 750 °C for 8 h prior to the electrochemical measurements. An electrochemical interface (Solartron 1287) and an impedance/gain phase analyzer (Solartron 1260) were adopted for the measurements. The initial EIS in wet H2 (with 3% H2O) or wet CH4 (with 3% H2O), and current density–voltage–power density (I–V–P) curves in wet CH4 were obtained at 600–750 °C. The carbon deposition resistant performance of the anode was studied in wet CH4 (with 3% H2O) under OCV at 750 °C.

Phase composition was examined using X-ray diffraction (XRD, XRD-7000). Scanning electron microscopy (SEM, GeminiSEM300), environmental scanning electron microscopy (ESEM, Quanta 200), and electron probe microanalysis (EPMA-8050G) were used to analyze the morphology and composition. Raman spectrometer (LabRAM HR800) was used to detect carbon deposition.

Acknowledgments

The authors thank the financial support from the National Key Research & Development Project (2016YFE0126900), the Natural Science Foundation of China (U1601207 and 51672095), and Hubei Province (2018AAA057). The assistance of Analytical and Testing Center of Huazhong University of Science and Technology for providing SEM and XRD characterizations is also appreciated.

The authors declare no competing financial interest.

References

  1. Timurkutluk B.; Timurkutluk C.; Mat M. D.; Kaplan Y. A review on cell/stack designs for high performance solid oxide fuel cells. Renewable Sustainable Energy Rev. 2016, 56, 1101–1121. 10.1016/j.rser.2015.12.034. [DOI] [Google Scholar]
  2. Lu Y.; Cai Y.; Souamy L.; Song X.; Zhang L.; Wang J. Solid oxide fuel cell technology for sustainable development in China: An over-view. Int. J. Hydrogen Energy 2018, 43, 12870–12891. 10.1016/j.ijhydene.2018.05.008. [DOI] [Google Scholar]
  3. Jiang S. P.; Chan S. H. A review of anode materials development in solid oxide fuel cells. J. Mater. Sci. 2004, 39, 4405–4439. 10.1023/B:JMSC.0000034135.52164.6b. [DOI] [Google Scholar]
  4. Tsipis E. V.; Kharton V. V. Electrode materials and reaction mechanisms in solid oxide fuel cells: a brief review. J. Solid State Electrochem. 2008, 12, 1367–1391. 10.1007/s10008-008-0611-6. [DOI] [Google Scholar]
  5. Kirtley J.; Singh A.; Halat D.; Oswell T.; Hill J. M.; Walker R. A. In Situ Raman Studies of Carbon Removal from High Temperature Ni–YSZ Cermet Anodes by Gas Phase Reforming Agents. J. Phys. Chem. C 2013, 117, 25908–25916. 10.1021/jp408192e. [DOI] [Google Scholar]
  6. He H.; Hill J. M. Carbon deposition on Ni/YSZ composites exposed to humidified methane. Appl. Catal., A 2007, 317, 284–292. 10.1016/j.apcata.2006.10.040. [DOI] [Google Scholar]
  7. Singh A.; Islam S.; Buccheri M.; Hill J. Influence of experimental conditions on reliability of carbon tolerance studies on Ni/YSZ SOFC anodes operated with methane. Fuel Cells 2013, 13, 703–711. 10.1002/fuce.201200231. [DOI] [Google Scholar]
  8. Kumar M.; Ando Y. Chemical vapor deposition of carbon nanotubes: a review on growth mechanism and mass production. J. Nanosci. Nanotechnol. 2010, 10, 3739–3758. 10.1166/jnn.2010.2939. [DOI] [PubMed] [Google Scholar]
  9. Ideris A.; Croiset E.; Pritzker M.; Amin A. Direct-methane solid oxide fuel cell (SOFC) with Ni-SDC anode-supported cell. Int. J. Hydrogen Energy 2017, 42, 23118–23129. 10.1016/j.ijhydene.2017.07.117. [DOI] [Google Scholar]
  10. Toebes M. L.; Bitter J. H.; Van Dillen A. J.; de Jong K. P. Impact of the structure and reactivity of nickel particles on the catalytic growth of carbon nanofibers. Catal. Today 2002, 76, 33–42. 10.1016/S0920-5861(02)00209-2. [DOI] [Google Scholar]
  11. Ruiz-Morales J. C.; Canales-Vázquez J.; Savaniu C.; Marrero-López D.; Zhou W.; Irvine J. T. Disruption of extended defects in solid oxide fuel cell anodes for methane oxidation. Nature 2006, 439, 568–571. 10.1038/nature04438. [DOI] [PubMed] [Google Scholar]
  12. Da Silva F. S.; de Souza T. M. Novel materials for solid oxide fuel cell technologies: A literature review. Int. J. Hydrogen Energy 2017, 42, 26020–26036. 10.1016/j.ijhydene.2017.08.105. [DOI] [Google Scholar]
  13. Weston M.; Metcalfe I. La0.6Sr0.4Co0.2Fe0.8O3 as an anode for direct methane activation in SOFCs. Solid State Ionics 1998, 113–115, 247–251. 10.1016/S0167-2738(98)00377-4. [DOI] [Google Scholar]
  14. Tao S.; Irvine J. T. A redox-stable efficient anode for solid-oxide fuel cells. Nat. Mater. 2003, 2, 320–323. 10.1038/nmat871. [DOI] [PubMed] [Google Scholar]
  15. Hui S.; Petric A. Conductivity and stability of SrVO3 and mixed perovskites at low oxygen partial pressures. Solid State Ionics 2001, 143, 275–283. 10.1016/S0167-2738(01)00870-0. [DOI] [Google Scholar]
  16. Li M.; Hua B.; Jiang S. P.; Pu J.; Chi B.; Jian L. BaZr0.1Ce0.7Y0.1Yb0.1O3−δ as highly active and carbon tolerant anode for direct hydrocarbon solid oxide fuel cells. Int. J. Hydrogen Energy 2014, 39, 15975–15981. 10.1016/j.ijhydene.2014.01.132. [DOI] [Google Scholar]
  17. Zhu W.; Deevi S. A review on the status of anode materials for solid oxide fuel cells. Mater. Sci. Eng., A 2003, 362, 228–239. 10.1016/S0921-5093(03)00620-8. [DOI] [Google Scholar]
  18. Sholklapper T. Z.; Radmilovic V.; Jacobson C. P.; Visco S. J.; De Jonghe L. C. Synthesis and stability of a nanoparticle-infiltrated solid oxide fuel cell electrode. Electrochem. Solid-State Lett. 2007, 10, B74–B76. 10.1149/1.2434203. [DOI] [Google Scholar]
  19. Jiang S. P. Nanoscale and nano-structured electrodes of solid oxide fuel cells by infiltration: advances and challenges. Int. J. Hydrogen Energy 2012, 37, 449–470. 10.1016/j.ijhydene.2011.09.067. [DOI] [Google Scholar]
  20. Liu Z.; Liu B.; Ding D.; Liu M.; Chen F.; Xia C. Fabrication and modification of solid oxide fuel cell anodes via wet impregnation/infiltration technique. J. Power Sources 2013, 237, 243–259. 10.1016/j.jpowsour.2013.03.025. [DOI] [Google Scholar]
  21. Li M.; Hua B.; Luo J.-l.; Jiang S. P.; Pu J.; Chi B.; Jian L. Carbon-tolerant Ni-based cermet anodes modified by proton conducting yttrium- and ytterbium-doped barium cerates for direct methane solid oxide fuel cells. J. Mater. Chem. A 2015, 3, 21609–21617. 10.1039/C5TA06488K. [DOI] [Google Scholar]
  22. Zhu T.; Troiani H. E.; Mogni L. V.; Han M.; Barnett S. A. Ni-substituted Sr(Ti,Fe)O3 SOFC anodes: achieving high performance via metal alloy nanoparticle exsolution. Joule 2018, 2, 478–496. 10.1016/j.joule.2018.02.006. [DOI] [Google Scholar]
  23. Du Z.; Zhao H.; Yi S.; Xia Q.; Gong Y.; Zhang Y.; Cheng X.; Li Y.; Gu L.; Świerczek K. High-performance anode material Sr2FeMo0.65Ni0.35O6−δ with in situ exsolved nanoparticle catalyst. ACS Nano 2016, 10, 8660–8669. 10.1021/acsnano.6b03979. [DOI] [PubMed] [Google Scholar]
  24. Song Y.; Wang W.; Ge L.; Xu X.; Zhang Z.; Julião P. S. B.; Zhou W.; Shao Z. Rational design of a water-storable hierarchical architecture decorated with amorphous barium oxide and nickel nanoparticles as a solid oxide fuel cell anode with excellent sulfur tolerance. Adv. Sci. 2017, 4, 1700337 10.1002/advs.201700337. [DOI] [PMC free article] [PubMed] [Google Scholar]
  25. Zhang S.-L.; Wang H.; Lu M. Y.; Zhang A.-P.; Mogni L. V.; Liu Q.; Li C.-X.; Li C.-J.; Barnett S. A. Cobalt-substituted SrTi0.3Fe0.7O3−δ: a stable high-performance oxygen electrode material for intermediate-temperature solid oxide electrochemical cells. Energy Environ. Sci. 2018, 11, 1870–1879. 10.1039/C8EE00449H. [DOI] [Google Scholar]
  26. Lefebvre-Joud F.; Gauthier G.; Mougin J. Current status of proton-conducting solid oxide fuel cells development. J. Appl. Electrochem. 2009, 39, 535–543. 10.1007/s10800-008-9744-7. [DOI] [Google Scholar]
  27. Li M.; Hua B.; Pu J.; Chi B.; Jian L. Electrochemical performance and carbon deposition resistance of M-BaZr0.1Ce0.7Y0.1Yb0.1O3-δ (M = Pd, Cu, Ni or NiCu) anodes for solid oxide fuel cells. Sci. Rep. 2015, 5, 7667 10.1038/srep07667. [DOI] [PMC free article] [PubMed] [Google Scholar]
  28. Nagamori M.; Shimonosono T.; Sameshima S.; Hirata Y.; Matsunaga N.; Sakka Y. Densification and Cell Performance of Gadolinium-Doped Ceria (GDC) Electrolyte/NiO-GDC Anode Laminates. J. Am. Ceram. Soc. 2009, 92, S117–S121. 10.1111/j.1551-2916.2008.02646.x. [DOI] [Google Scholar]
  29. Triantafyllopoulos N. C.; Neophytides S. G. Dissociative adsorption of CH4 on NiAu/YSZ: the nature of adsorbed carbonaceous species and the inhibition of graphitic C formation. J. Catal. 2006, 239, 187–199. 10.1016/j.jcat.2006.01.021. [DOI] [Google Scholar]
  30. Liu Q.; Dong X.; Xiao G.; Zhao F.; Chen F. A novel electrode material for symmetrical SOFCs. Adv. Mater. 2010, 22, 5478–5482. 10.1002/adma.201001044. [DOI] [PubMed] [Google Scholar]
  31. Chiodelli G.; Malavasi L. Electrochemical open-circuit voltage (OCV) characterization of SOFC materials. Ionics 2013, 19, 1135–1144. 10.1007/s11581-013-0843-z. [DOI] [Google Scholar]
  32. Liu Y.; Chi B.; Pu J.; Li J. Performance degradation of impregnated La0.6Sr0.4Co0.2Fe0.8O3+Y2O3 stabilized ZrO2 composite cathodes of intermediate temperature solid oxide fuel cells. Int. J. Hydrogen Energy 2012, 37, 4388–4393. 10.1016/j.ijhydene.2011.11.151. [DOI] [Google Scholar]

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