Next Article in Journal
Influencing the Crystalline Domains of Poly(vinylidenedifluoride) Composites Using Fluorinated Silica Nanoparticles as Drop-In Modifiers
Previous Article in Journal
Multielement Determination in Turmeric (Curcuma longa L.) Using Different Digestion Methods
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Molecules
Volume 27
Issue 23
10.3390/molecules27238396
molecules-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

Solid Oxide Cells with Phase-Inversion Tape-Casted Hydrogen Electrode and SrSc0.175Nb0.025Co0.8O3−δ Oxygen Electrode for High-Performance Reversible Power Generation and Hydrogen Production

by
Meiting Yang
1,
Changjiang Yang
1,
Mingzhuang Liang
1,
Guangming Yang
1,*,
Ran Ran
1,
Wei Zhou
1 and
Zongping Shao
1,2
1
State Key Laboratory of Materials-Oriented Chemical Engineering, College of Chemical Engineering, Nanjing Tech University, Nanjing 211816, China
2
WA School of Mines: Minerals, Energy and Chemical Engineering, Curtin University, Perth, WA 6845, Australia
*
Author to whom correspondence should be addressed.
Molecules 2022, 27(23), 8396; https://doi.org/10.3390/molecules27238396
Submission received: 8 October 2022 / Revised: 22 November 2022 / Accepted: 24 November 2022 / Published: 1 December 2022
(This article belongs to the Special Issue Green Hydrogen—Perspectives from the Young Investigators’ Point of View)
Browse Figures
Versions Notes

Abstract

:
Solid oxide cells (SOCs) have been considered as a promising energy conversion and storage device. However, state-of-the-art cells’ practical application with conventionally fabricated Ni-(Y2O3)0.08(ZrO2)0.92 (YSZ) cermet hydrogen electrode and La0.8Sr0.2MnO3 perovskite oxygen electrode is strongly limited by the unsatisfactory performance. Instead, new advances in cell materials and fabrication techniques that can lead to significant performance enhancements are urgently demanded. Here, we report a high-performance reversible SOC that consisted of a combination of SrSc0.175Nb0.025Co0.8O3−δ (SSNC) and phase-inversion tape-casted Ni-YSZ, which served as the oxygen and hydrogen electrode, respectively. The hydrogen electrode synthesized from phase-inversion tape-casting showed a high porosity of 60.8%, providing sufficient active sites for hydrogen oxidation in the solid oxide fuel cell (SOFC) mode and H2O electrolysis in the solid oxide electrolysis cell (SOEC) mode. Accordingly, it was observed that the maximum power density of 2.3 W cm−2 was attained at 750 °C in SOFC mode and a current density of −1.59 A cm−2 was obtained at 1.3 V in SOEC mode. Hence, these results reveal that the simultaneous optimization of oxygen and hydrogen electrodes is a pragmatic strategy that improves the performance of SOCs, which may significantly accelerate the commercialization of such an attractive technology.

Graphical Abstract

1. Introduction

With the rapid consumption of fossil fuels and aggravation of the global climate crisis, innovative technologies must be developed to utilize renewable energies such as solar and wind power effectively. Considering the intermittent nature of renewable energy, energy storage technologies are needed to achieve high-quality renewable energy use. Hydrogen energy has attracted widespread attention as an energy carrier due to having high calorific value and no pollution [1,2,3]. In the hydrogen production process, using a solid oxide electrolysis cell (SOEC) for water electrolysis has been extensively studied owing to its high energy efficiency and ease of product separation and modular operation [4,5,6,7]. Noteworthily, solid oxide cells (SOCs) can operate in two modes, regarded as SOEC and solid oxide fuel cell (SOFC), meaning that energy can be efficiently stored and regenerated by alternately switching between the different modes [8,9,10]. The integration of hydrogen production, SOEC technology utilizing renewable energy, and SOFC technology generating power from hydrogen will provide a sustainable renewable energy-based clean energy system for the future.
Recently, many researchers have discovered that the oxygen electrode plays a critical role in developing high-performance and stable SOCs [11,12,13,14]. In the SOFC mode, the oxygen electrode is used as an electrocatalyst for an oxygen reduction reaction (ORR), whereas it acts as an oxygen evolution reaction (OER) catalyst in the SOEC mode. An ideal oxygen electrode for SOCs should have good activity and durability for both the ORRs and OERs. Cobalt-based perovskite oxides such as La0.6Sr0.4Co0.2Fe0.8O3−δ (LSCF) are the most intensively investigated oxygen electrodes in SOCs [12,15]. Unfortunately, these materials have not exhibited excellent ORR activity in the SOFC mode, especially at low to intermediate temperatures. Moreover, it was found that the effects of water vapor and chromium poisoning cannot be negligible in terms of the electrochemical performance of the LSCF electrode in the SOEC mode, resulting in rapid performance degradation [16,17]. Many works have reported that oxygen electrode performance is related to many factors, such as surface area, oxygen vacancy concentration, and oxygen transport rates. Several perovskite oxides derived from the SrCoO3−δ parent oxide, such as Ba0.5Sr0.5Co0.8Fe0.2O3−δ (BSCF) and BaCo0.4Fe0.4Zr0.1Y0.1O3−δ (BCFZY), have showed superior ORR activity under intermediate temperatures [18,19,20,21]; for instance, this result was observed that the BSCF electrode has a lower area-specific resistance (ASR) of 0.1 Ω cm2 when working at 600 °C in the SOFC mode and at a current density of −0.45 A cm−2 at 850 °C in the SOEC mode [18,19]. Recently, Sc and Nb co-doped perovskite oxide denominated SrSc0.175Nb0.025Co0.8O3−δ (SSNC) was demonstrated to be an outstanding electrode for the SOFC mode. Moreover, the single cells fabricated by SSNC can achieve a maximum power density of 910 mW cm−2 at 500 °C with hydrogen fuel [22]. However, the OER performance of SSNC in the SOEC mode has not been further studied.
Apart from the oxygen electrode, there is another type of excellent electrocatalyst, the hydrogen electrode, that plays a crucial role concerning both hydrogen electro-oxidation in the SOFC mode and water splitting in the SOEC mode. Recently, considerable attention has also been paid to the development of a practical hydrogen electrode for SOCs [23,24,25,26,27]. Ni-(Y2O3)0.08(ZrO2)0.92 (YSZ) composite is the state-of-the-art anode for the SOFC mode due to its favorable catalytic activity for hydrogen electro-oxidation, high conductivity, good thermomechanical compatibility with the YSZ electrolyte, and relatively low cost, which is also widely used in SOCs. However, the hydrogen electrode prepared by the conventional tape-casting method usually showed low porosity, thus introducing massive polarization resistance in the SOEC mode, especially under a high polarization current. This suggests that optimizing the porosity of electrode may contribute to increase the SOC’s performance. Some studies have applied a phase-inversion tape-casting technique with NMP as a solvent, PESF as a binder, and PVP as a dispersant to improve the morphology and porosity of the Ni-based hydrogen electrode [28,29,30,31].
In this study, we conducted the simultaneous improvement of both oxygen and hydrogen electrodes to achieve a high performance of SOCs. It was demonstrated that SSNC is an excellent cathode for SOFC, and for the first time, we proved that SSNC is also a suitable oxygen electrode in the SOC mode; thus, it was adopted as the oxygen electrode in the SOCs. We also report a Ni-YSZ hydrogen electrode with a honeycomb-like structure synthesized by a novel phase-inversion tape-casting method and having a much-increased electrode porosity. Combining the SSNC oxygen electrode and Ni-YSZ hydrogen electrode casted by phase-inversion tape has a remarkable performance in both two modes: a maximum power density of 2.3 W cm−2 at 750 °C in the SOFC mode and a current density of −1.59 A cm−2 at 1.3 V in the SOEC mode, respectively.

2. Results and Discussion

2.1. Microstructure of Hydrogen Electrode

It was reported that the hydrogen electrode’s porosity had a considerable influence in terms of the electrode performance, and a highly porous electrode microstructure could result in an improvement of the electrochemical performance of single cells [32,33,34,35]. Here, to emphasize the importance of microstructure optimization regarding the performance of hydrogen electrodes in SOFCs, two types of Ni-YSZ hydrogen electrodes with different structures were fabricated by the tape-casting and phase-inversion tape-casting methods, respectively.
The cross-sectional FE-SEM images of two hydrogen electrodes calcined at 1400 °C for 5 h before tests are shown in Figure 1a,b for the tape-casted electrode and Figure 1c,d for the electrode fabricated from the phase-inversion tape-casted electrode, respectively. Obviously, the hydrogen electrode produced by the conventional tape-casting method showed poor porosity after calcining at 1400 °C, and there are only a few 1–2 μm tortuous and irregular pores (Figure 1a,b). The porosity of this electrode after the reduction would be mainly attributed to the contraction due to the reduction from NiO to Ni. However, for the electrode prepared from the phase-inversion tape-casting method, in addition to some unevenly distributed large pores (30–250 μm), there are also many uniformly distributed small pores (~10 μm), which takes after the honeycomb structure (Figure 1c,d). Such honeycomb-type pores were not observed in the electrodes prepared by others based on the similar phase-inversion tape-casting method. Such a difference could result from the different casting solvents used in the phase-inversion tape-casting processes. Many researchers have obtained finger-like macroporous structures by using N-Methyl pyrrolidone (NMP) as a solvent [28,29,30,31]. It is known that NMP is an oily solvent, which slowly exchanges with water during the phase-inversion process and causes finger-like macropore formations. In this study, ethanol and xylene were used as the solvents. It is well-known that ethanol is readily miscible with water; thus, finger-like macropores did not appear. Meanwhile, due to xylene’s presence, a regular and ordered honeycomb structure can be formed if H2O entered the casting tape (Figure S1). Such a conclusion was further verified by thermogravimetric-mass spectrometric (TG-MS) testing of the casted tapes prepared by two different methods; the results are shown in Figure S2. Within the temperature range of 50–1000 °C, the calculated weight losses of the conventional casted tape and the phase-inversion casted tape were 16.2% and 14.7%, respectively (Figure S2a). In the same test interval, the conventional casted tape released slightly more water than prepared by the phase-inversion method, which was mainly caused by the immersion of the casted tape in water and not being thoroughly dried. However, the conventional casted tape released significantly more CO2 (Figure S2b) because the ethanol was entirely dissolved in the H2O, and part of the xylene was exchanged with H2O during the phase inversion process. Jin et al. also used glycol as a non-solvent and NMP as a solvent to obtain honeycomb-like pores in the electrode by the phase-inversion method; unfortunately, these honeycomb structures were destroyed after the electrochemical test [36]. Hence, there is no doubt that the ordered honeycomb-like structure of the hydrogen electrode would benefit the mass transfer of fuels and by-products formation in the operation of SOCs [34].
The surface morphology of the two hydrogen electrodes was also examined with the results shown in Figure S3. Unlike the dense hydrogen electrode prepared by the tape-casting method (Figure S3a,b), there were many pores with a size of ~5 μm on the surface of the hydrogen electrode generated by the phase-inversion tape-casting method (Figure S3c,d). Such rich pores facilitated the modification of the hydrogen electrode using an impregnation method. The electrode should usually be pre-reduced to introduce sufficient pores before conducting the solution-impregnated modification to modify the electrode through impregnation [37,38]. Due to the rich pores, the hydrogen electrode made by the phase-inversion tape-casting method can be directly applied to the surface modification through solution impregnation, thus greatly simplifying the preparation process and effectively reducing the fabrication cost. To verify the wettability of the surface on different hydrogen electrodes, a drop of water was dropped on the different hydrogen electrodes surface simultaneously, and the images were taken after 3 s (Figure S4). Obviously, the water on the surface of the phase-inversion tape-casting hydrogen electrode was wholly impregnated into the electrode, while that on the surface of the conventional tape-casting hydrogen electrode was hardly absorbed due to the low porosity.
The cross-sectional FE-SEM images of the two different hydrogen electrodes fabricated by the traditional tape-casting and phase-inversion tape-casting methods after the cell test (reduced) were also conducted. Under the cast slurry with the same thickness, the hydrogen electrodes’ thickness increased from the initial ~500 μm to ~750 μm before and after the phase inversion (Figure 2a,b). The variation in the thickness of the hydrogen electrode also proves that the phase-inversion tape-casting method is a remarkably simple and effective method for improving electrode porosity. Because NiO was usually reduced to Ni under a reducing atmosphere, the hydrogen electrode produced by the conventional tape-casting method also clearly demonstrated a connected porous structure (Figure 2c,e), and there were also small micropores between the NiO and YSZ particles. Except for the micropores in the space of different Ni and YSZ particles, the hydrogen electrode prepared by the phase-inversion method also shows sufficient ordered honeycomb-structure pores with a size of ~10 μm (Figure 2d,f). Therefore, the hydrogen electrode prepared by the phase inversion method demonstrated a better continuous transitional microstructure, which will facilitate fuel and product transportation and electrode electrochemical reactions.
The pore size distribution of Ni-YSZ substrate was evaluated through mercury porosimetry measurement, with the results shown in Figure 3. Only one primary pore size was detected in the electrode prepared from the conventional tape casting method, i.e., pore size of 0.1–1 μm in diameter, and such pores were mainly attributed to the void space between the Ni and YSZ particles. However, there are two domains of pores in the electrode synthesized by the phase-inversion tape-casting method: one corresponds to the void space of Ni and YSZ particles (0.1–1 μm), and the other relates to the effective small pores with a diameter between 1 and 10 μm explicitly introduced by the phase-inversion method. These results agree well with previous FE-SEM observations (Figure 2). The total intruded volume and the porosity of the two different hydrogen electrodes are listed in Table S1. By using the phase-inversion method, the intruded volume in the electrode was increased from 0.067 to 0.24 cm3 g−1, and the porosity was also increased from 32.1% to 60.8%. In a previous work, Suzuki et al. reported that the porosity of a tubular SOFC was increased from 37% to 54% by tailoring the calcination temperatures, thus achieving an effective improvement in the peak power density from 0.2 to 1 W cm−2 [34]. Therefore, the electrode synthesized by the phase-inversion tape-casting method with high porosity is expected to deliver a higher electrochemical performance in SOCs.
To further prove that the nickel and YSZ in the prepared Ni-YSZ hydrogen electrode by the phase-inversion tape-casting method were evenly distributed, a STEM-EDX analysis was performed for the reduced hydrogen electrode at 750 °C for 5 h, with the typical images shown in Figure 4. There was no apparent aggregation of Ni or YSZ particles, and the Ni and YSZ particles were closely connected, effectively forming the continuous oxygen ion diffusion path (YSZ) and electron conduction path (Ni) (Figure 4b–e). The prepared Ni-YSZ electrode’s elemental composition was further illustrated by the EDX test (Figure 4f), which is consistent with the initial element ratio of Ni and YSZ.

2.2. Water Resistance of Oxygen Electrode

It is crucial for SOCs to have high activity concerning oxygen reduction reactions (ORRs) and oxygen evolution reactions (OERs) and prolonged durability of the oxygen electrode when working at low-to-intermediate temperatures. Zhou et al. have confirmed that the perovskite material SrSc0.175Nb0.025Co0.8O3−δ (SSNC) is an excellent candidate because of its relatively high ORR activity and low activation energy, which was enhanced to 100% at 500 °C relative to the benchmark oxygen electrode of BSCF [22]. Zhang et al. also confirmed that SSNC had a higher ORR activity and CO2-resistance than BSCF [39]. To further confirm the high activity of SSNC, an O2-TPD test was carried out. As shown in Figure S5, during the programmed increase of temperature, the thermal reduction of B-site cations to a lower oxidation state occurs, along with the oxidation of O2− to O2, which is finally released into the surrounding atmosphere (via flowing inert gas). It is evident that the peak area of SSNC is much higher than that of BSCF, indicating that SSNC has more variable oxygen vacancies than BSCF [39]. However, in the SOEC mode, because a large amount of water vapor is introduced into the hydrogen electrode, which may be penetrated by the oxygen electrode, and a stable phase structure and micromorphology under an absolute water pressure is vital for oxygen electrodes for SOCs. Figure 5 shows the XRD patterns of the BSCF and SSNC before and after treatment in 10% H2O-Ar at 750 °C for 5 h. Obviously, a significant impurity peak appeared at the 2-theta position at about 26° in the BSCF sample (Figure 5a). Yan et al. found the presence of a OH group after the treatment of BSCF in an atmosphere containing H2O [40]. Wang et al. also confirmed that Ba(OH)2 could be formed on Ba0.9Co0.7Fe0.2Nb0.1O3−δ (BCFN) after treatment under an atmosphere containing H2O [41]. During the electrolysis process, the presence of Ba(OH)2 on the BSCF oxygen electrode’s surface may inhibit the oxygen evolution process. Nevertheless, for the SSNC perovskite, no impurity peaks appeared after treatment in 10% H2O-Ar atmosphere, indicating its high resistance to water poisoning (Figure 5b). This is mainly because the alkalinity of the Ba element is greater than that of the Sr element, so water reacts more easily with BSCF to form Ba(OH)2. Zhang et al. found that CO2 is more likely to poison BSCF due to Ba’s strong alkalinity, while SSNC is much more CO2-resistant than BSCF [39].
To further verify the different effects of H2O on the SSNC and BSCF perovskites, the electrode microstructure was examined after the water treatment. In our previous work, the surface roughness of BSCF and SSCN samples before treatment is close to each other with no significant difference, which was illustrated by scanning electron microscopy and atomic force microscopy [39]. As shown in Figure 6a,b, the surface of SSNC perovskite was smooth without the presence of any impurities, while there were large amounts of impurities with a particle size distribution of 100–200 nm emerging on the surface of BSCF perovskite (Figure 6c,d). According to the XRD results, such impurities on the BSCF surface were mainly Ba(OH)2. Therefore, in addition to the higher bulk oxygen diffusion rate and oxygen reduction activity than BSCF, SSNC also has a stronger resistance towards water poisoning, making it a more promising oxygen electrode for SOCs compared with BSCF.

2.3. SOFC Mode

Cell 1 was first tested in the SOFC mode and compared with the other two cells listed in Table 1. Figure 7a–c exhibits the I-V and I-P curves where three cells with different compositions work at various temperatures of 650–750 °C in the atmosphere consisting of humidified H2 as the fuel and ambient air as the oxidant. The open-circuit voltages (OCVs) of Cell 1, Cell 2, and Cell 3 at 750 °C were 1.06, 1.06, and 1.03 V, respectively, which indicated that YSZ electrolyte could be densified and the porous hydrogen electrode prepared by the phase-inversion method did not affect the compactness of the three cells. In comparison, Huang et al. reported a cell with finger-like large pores on the hydrogen electrode, which was prepared via the phase-inversion tape-casting method and showed an OCV of only 1.00 V at 750 °C [29]. Significantly, the peak power densities (PPDs) of the three cells were 1.44, 1.70, 1.36 W cm−2 at 700 °C, respectively. Obviously, the power densities of these cells produced by the phase-inversion tape-casting method are superior to those synthesized through the traditional tape-casting method when compared under similar testing conditions. Similarly, the SSNC cathode cells had higher power densities than those that made up of BSCF cathode. The detailed PPDs of the three cells at the specific operating temperatures are shown in Figure 7d, suggesting that the performance in the SOFC mode was enhanced by optimizing the microstructure of the hydrogen electrode and the reactivity of the oxygen electrode. The performances of various single cells containing Ni-based hydrogen electrodes, YSZ electrolyte, and other well-known oxygen electrodes are compared in Table 2 [28,29,37,42,43,44,45,46,47,48,49,50,51]. It was found that the cells consisted of a hydrogen electrode with a honeycomb-like structure, and the oxygen electrode with SSNC cathode demonstrated the best electrochemical performance.

2.4. SOEC Mode

Figure 8a–c presents the temperature-dependent I-V curves of the three different cells for electrolysis. Within the test period, the volume flow ratio of H2O/H2 was maintained at 1:1, and the test voltages started from OCVs to −1.6 V with a current sweeping rate of 50 mA s−1. Thus, it was necessary to utilize Faraday’s law to calculate the H2 production rate at the corresponding current density. As seen in the following, Faraday’s law is ΔNH2 = I/2F, where ΔNH2 is the H2 production rate (mL cm−2 h−1), and I and F is the current (A) and Faraday’s constant (C), respectively [52,53]. When the thermo-neutral voltage for steam electrolysis is 1.3 V, the current densities of three cells are −1.43, −1.59, and −1.35 A cm−2 at 750 °C, and the corresponding derived H2 production rate are 597.6, 664.5, and 564.1 mL cm−2 h−1 at 750 °C, respectively. Meanwhile, it can be seen that Cell 1 showed an obvious polarization phenomenon at 750 °C, which cannot be seen for the other two cells. This is due to the water electrolysis reaction at higher temperatures needing much more reactant with a high concentration of water compared with that of lower temperatures, and the insufficient porosity (32.1%) of Cell 1 cannot satisfy the demands for water diffusion. Therefore, Cell 1 showed an obvious concentration polarization phenomenon at 750 °C. However, the phase-inversion tape-casting hydrogen electrodes had good porosity (60.8%); the concentration polarization phenomenon cannot be seen in the I-V curves of Cell 2 and Cell 3. Figure 8d illustrates the detailed current densities of three cells at the operating voltage and temperature. It was found the electrolysis performance of Cell 2 is superior to Cell 1 and Cell 3, implying that the electrolysis performance of cell was successfully strengthened by combining the phase-inversion tape-casted hydrogen electrode with the SSNC oxygen electrode. Moreover, the electrolysis performances of various single cells with the Ni-based hydrogen electrodes, YSZ electrolyte, and other oxygen electrodes are compared in Table 3 [30,44,46,48,49,50,54,55,56,57]. Again, SOECs consisted of the hydrogen electrode with a honeycomb-like structure and the SSNC oxygen electrode show the best electrochemical performance.
To further research the electrochemical performance, it is essential to exert the electrochemical impedance spectra (EIS) to measure the impedance value of the SOECs, and the final results of this investigation are shown in Figure S6a–c. The polarization resistance (Rp) of Cell 2 is smaller than those of the other two cells under the same conditions (Figure S6d). These results are consistent with the SOC performance. Simultaneously, the three cells’ ohmic resistances (Ro) are basically the same, indicating that the three cells’ electrolyte thicknesses are almost the same.

2.5. Stability

It is known that the easy agglomeration of Ni nanoparticles at high temperatures is a severe problem during SOEC operation [58,59]. The accumulation of Ni crystal grains at high temperature may be accelerated owing to the relatively low melting point of metallic Ni and the adverse interaction between YSZ and Ni, which means that it could seriously damage the contact surface between the Ni metal and the electrolyte substrate. This is the main reason why it reduced electronic conductivity and declined the area of the three-phase boundary. Accordingly, the cell performance has been expected to deteriorate over a long time, which results from increasing polarization and ohmic impedances. The durability of Cell 2 was tested in both the SOFC and SOEC modes. Figure 9 shows the variation of cell voltage concerning operation time in the alternating operation mode for a period of 50 h under −0.5 A cm−2 for the electrolysis mode and then 50 h of operation at 0.5 A cm−2 for the fuel cell mode with a total period of 200 h. Although the voltage slightly increased from 1.3 V to 1.39 V during the first 50 h under the electrolysis mode, the voltage returned to 1.31 V when the cell was electrolyzed for the second 50 h. SOCs based on Ni-based hydrogen electrodes can effectively suppress the electrolytic performance by switching the SOEC and SOFC modes. In the SOFC mode, no significant performance degradation was observed in two different sets of 50 h operation. Therefore, the SOCs with the phase-inversion tape-casted hydrogen electrode and SSNC oxygen electrode have a good stability and potential application prospect.
After the stability test, the cross-sectional FE-SEM image of Cell 2 (Ni-YSZ|YSZ|SDC|SSNC) was conducted, as shown in Figure S7, demonstrating that the thickness of the YSZ electrolyte, SDC barrier layer, and SSNC oxygen electrode were ~4.5 μm, ~2 μm, and ~9 μm, respectively. The thin YSZ electrolyte layer was still dense without the appearance of obvious holes. Simultaneously, the SSNC oxygen electrode and electrolyte did not show any delamination after 200 h of testing.

3. Materials and Methods

3.1. Powder Preparation

SrSc0.175Nb0.025Co0.8O3−δ (SSNC) oxide powder was prepared by a standard solid-state reaction method. In detail, according to the nominal composition of the perovskite oxides, stoichiometric amounts of SrCO3, Sc2O3, Nb2O5, and Co3O4 were weighted and mixed with ethanol in a ball milling machine for 30 min. After drying at 180 °C for 5 h, the precursor powder was calcined at 1200 °C for 10 h in air to obtain pure SSNC perovskite power. Using the detailed procedure presented in the literature, a classic EDTA-citric acid complexing sol-gel process was introduced and used to synthesize the oxygen electrode materials, Ba0.5Sr0.5Co0.8Fe0.2O3−δ (BSCF) perovskite oxide [32]. Meanwhile, Sm0.2Ce0.8O1.9 (SDC) oxide powder, acting as a buffer layer of the YSZ electrolyte of SOCs in this study, was synthesized by a hydrothermal process [33], where the YSZ was a commercial product purchased from Tosoh, Japan.

3.2. Single Cell Preparation

A hydrogen electrode-supported half-cell was synthesized through the phase-inversion tape-casting method. Usually, the single cell consists of the Ni-YSZ cermet hydrogen electrode, the YSZ electrolyte (SDC as a barrier), and the SSNC or BSCF oxygen electrode. The phase-inversion tape-casting method was introduced to create the unreduced NiO-YSZ (NiO and YSZ in a mass ratio of 6:4) hydrogen electrode. In detail, NiO and YSZ oxide powders were mixed well through ball milling at a mass ratio of 6:4, and a proper amount of ethanol and xylene were added during the ball milling process as solvents; fish oil was added as the dispersing agent. The milling was first conducted in a planetary ball mill for 24 h to ensure sufficient dispersion between the NiO and YSZ. Then, a second feeding was performed. An appropriate amount of polyvinyl butyral ester as a binder and dioctyl phthalate and polyethylene glycol 400 as plasticizers was added to the solution, which was ball remixed for another 24 h to obtain a slurry that would be used for subsequent tape-casting. The prepared hydrogen electrode mixture’s slurry was degassed for 5 min by the vacuum pump and casted with a 2 mm height gap. A part of the tape-casting hydrogen electrode was directly dried at room temperature for 24 h to prepare a traditional tape-casting hydrogen electrode, and the other part was directly immersed in water for 24 h to prepare a phase-inversion tape-casting hydrogen electrode. The detailed preparation process for the traditional tape-casting and phase-inversion tape-casting hydrogen electrodes was shown in Figure S1. A hydrogen electrode pellet was formed by punching the tape-casted film using a puncher with a 16 mm diameter. Through a 2 h heating process in air, the punched pellets were fired to 1000 °C at a heating rate of 1 °C min−1. The hydrogen electrode surface was sprayed with the prepared YSZ slurry, and the sprayed pellet continued to be calcined at 1400 °C for 5 h in air. Moreover, spraying the SDC slurry on the YSZ electrolyte uniformly and calcining it in air at 1300 °C for 5 h should not be negligible, as the formation of the SDC barrier layer was aimed at avoiding adverse phase reaction happening at the contact surface between the electrolyte and the oxygen electrode. Eventually, in order to fabricate the entire single cell, it was essential to uniformly spray the SSNC oxygen electrode slurry on the surface of the SDC layer, where the effective area was 0.45 cm2, and the layer was calcined in air at 900 °C for 2 h. In order to enhance the current collection effect, silver paste was brushed on the oxygen electrode surface. For the convenience of distinguishing different SOCs, the cells were named as follows: Cell 1, composed of a tape-casting hydrogen electrode and SSNC oxygen electrode; Cell 2, composed of a phase-inversion tape-casting hydrogen electrode and SSNC oxygen electrode; and Cell 3, composed of a phase-inversion tape-casting hydrogen electrode and BSCF oxygen electrode. The different structures of the three cells are listed in Table 1.

3.3. Characterization and Measurements

To verify the phase structure of the SSNC and BSCF perovskite powders, it was necessary to exert room temperature X-ray diffraction (XRD, D8 Advance, Bruker, Billerica, MA, USA) to characterize them. The microstructural features of the cell components were examined with the use of scanning electron microscopy (FE-SEM, HITACHI-S4800). Silver adhesive was used to seal and fix the prepared cell on the end of a tubular alumina, and silver ink and wires were applied to contact and collect electricity. Electrochemical impedance spectra (EIS) were measured under the frequency range of 0.1 Hz–100 kHz with a signal amplitude of 10 mV in an open-circuit voltage (OCV). When tested in the SOFC mode, the flow rate of pure hydrogen was set to 80 mL min−1 [STP] to supply the hydrogen electrode chamber; the oxygen electrode was exposed to the static ambient air, and the cells operated in the temperature range of 750–650 °C. The operating temperature selection is a balance between the performance and degradation factors. In the test of the SOEC mode, hydrogen and water vapor were pre-mixed at a volume ratio of 50:50 and then supplied into the hydrogen electrode chamber, where the oxygen electrode was directly exposed to the ambient air atmosphere. Furthermore, for the stability in both the SOFC and SOEC modes, these cells were tested at a fixed current density of ±0.5 A cm−2. Different from the single-cell performance test, in order to ensure that the collector did not sinter at high temperatures, a silver mesh was used as the single-cell collector for stability testing instead of silver paste, sacrificing part of the cell’s performance.

4. Conclusions

In this paper, solid oxide cells with a phase-inversion tape-casted hydrogen electrode and SrSc0.175Nb0.025Co0.8O3−δ oxygen electrode were successfully fabricated and investigated. The ordered honeycomb-like structure of the hydrogen electrode was formed through the phase-inversion method, which was favorable to fuel transfer and byproduct generation in SOCs. Compared with the benchmark BSCF oxygen electrode, the SSNC electrode had a stronger resistance to water poisoning. Combined with the phase-inversion tape-casted hydrogen electrode and SSNC oxygen electrode, the SOC achieved a peak power density of 2.3 W cm−2 in the SOFC mode and a high current density of −1.59 A cm−2 (at 1.3 V) in the SOEC mode at 750 °C. These results demonstrate that the SOC with a SrSc0.175Nb0.025Co0.8O3−δ oxygen electrode and phase-inversion tape-casted hydrogen electrode has promise in water splitting prospects at high temperatures.

Supplementary Materials

The following are available online at https://www.mdpi.com/article/10.3390/molecules27238396/s1. Figure S1: Schematic of the preparation processes for the tape-casting and phase-inversion tape-casting hydrogen electrodes; Figure S2: TG-DTA curves (a) and the MS analysis (b) for the tape-casting and phase-inversion tape-casting hydrogen electrodes before calcined. m/z = 18 for the H2O MS signal and m/z = 44 for the CO2 MS signal; Figure S3: SEM images of the surface of the tape-casting (a,b) and phase-inversion tape-casting (c,d) hydrogen electrodes calcined at 1400 °C for 5 h; Figure S4: Images of the tape-casting (a) and phase-inversion tape-casting (b) hydrogen electrodes calcined at 1400 °C for 5 h in 3 s when the water was dropped onto the surfaces; Figure S5: O2-TPD profiles of SSNC and BSCF powders in pure Ar atmosphere from 50 to 800 °C. The inset is the relative area of the SSNC and BSCF; Figure S6: Electrochemical impedance spectra of three cells at OCV at different temperatures with 50% H2O–50% H2. (a) Cell 1, (b) Cell 2, (c) Cell 3, (d) the polarization resistance and ohmic resistance of the three cells at different temperatures; Figure S7: Cross-section FE-SEM image of Cell 2 after the stability test. Table S1: Parameters of direct tape-casting and phase-inversion tape-casting hydrogen electrodes conducted by mercury intrusion.

Author Contributions

Conceptualization, G.Y. and M.Y.; methodology, M.Y. and C.Y.; software, M.L.; validation, M.Y. and G.Y.; formal analysis, G.Y.; investigation, R.R.; resources, W.Z.; data curation, Z.S.; writing—original draft preparation, M.Y.; writing—review and editing, M.Y. and G.Y.; visualization, R.R.; supervision, G.Y.; project administration, W.Z.; funding acquisition, G.Y. All authors have read and agreed to the published version of the manuscript.

Funding

This work was financially supported by the Natural Science Foundation of Jiangsu Province (BK20221312), State Key Laboratory of Clean Energy Utilization (ZJUCEU2021001).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interest.

Sample Availability

Samples of the compounds are not available from the authors.

References

  1. Li, C.; Zhu, D.; Cheng, S.; Zuo, Y.; Wang, Y.; Ma, C.; Dong, H. Recent research progress of bimetallic phosphides-based nanomaterials as cocatalyst for photocatalytic hydrogen evolution. Chin. Chem. Lett. 2022, 33, 1141–1153. [Google Scholar] [CrossRef]
  2. Yang, M.; He, F.; Zhou, C.; Dong, F.; Yang, G.; Zhou, W.; Shao, Z. New perovskite membrane with improved sintering and self-reconstructed surface for efficient hydrogen permeation. J. Membr. Sci. 2021, 620, 118980. [Google Scholar] [CrossRef]
  3. Parra, D.; Valverde, L.; Pino, F.J.; Patela, M.K. A review on the role, cost and value of hydrogen energy systems for deep decarbonisation. Renew. Sustain. Energy Rev. 2019, 101, 279–294. [Google Scholar] [CrossRef]
  4. Liu, Z.; Chen, Y.; Yang, G.; Yang, M.; Ji, R.; Song, Y.; Ran, R.; Zhou, W.; Shao, Z. One-pot derived thermodynamically quasi-stable triple conducting nanocomposite as robust bifunctional air electrode for reversible protonic ceramic cells. Appl. Catal. B Environ. 2022, 319, 121929. [Google Scholar] [CrossRef]
  5. Bi, L.; Boulfrad, S.; Traversa, E. Steam electrolysis by solid oxide electrolysis cells (SOECs) with proton-conducting oxides. Chem. Soc. Rev. 2014, 43, 8255–8270. [Google Scholar] [CrossRef]
  6. Lei, L.; Zhang, J.; Yuan, Z.; Liu, J.; Ni, M.; Chen, F. Progress report on proton conducting solid oxide electrolysis cells. Adv. Funct. Mater. 2019, 29, 1903805. [Google Scholar] [CrossRef]
  7. Kim, S.; Kim, G.; Manthiram, A. Dysprosium doping effects on perovskite oxides for air and fuel electrodes of solid oxide cells. J. Power Sources 2021, 497, 229873. [Google Scholar] [CrossRef]
  8. Liu, Z.; Cheng, D.; Zhu, Y.; Liang, M.; Yang, M.; Yang, G.; Ran, R.; Wang, W.; Zhou, W.; Shao, Z. Robust bifunctional phosphorus-doped perovskite oxygen electrode for reversible proton ceramic electrochemical cells. Chem. Eng. J. 2022, 450, 137787. [Google Scholar] [CrossRef]
  9. Zhang, W.; Zhou, Y.; Liu, E.; Ding, Y.; Luo, Z.; Li, T.; Kane, N.; Zhao, B.; Niu, Y.; Liu, Y.; et al. A highly efficient and durable air electrode for intermediate-temperature reversible solid oxide cells. Appl. Catal. B Environ. 2021, 299, 120631. [Google Scholar] [CrossRef]
  10. Liu, Y.; Shao, Z.; Mori, T. Development of nickel based cermet anode materials in solid oxide fuel cells–Now and future. Mater. Rep. Energy 2021, 1, 100003. [Google Scholar] [CrossRef]
  11. Yang, G.; Su, C.; Shi, H.; Zhu, Y.; Song, Y.; Zhou, W.; Shao, Z. Toward reducing the operation temperature of solid oxide fuel cells: Our past 15 years of efforts in cathode development. Energy Fuels 2020, 34, 15169–15194. [Google Scholar] [CrossRef]
  12. Xu, X.; Su, C.; Shao, Z. Fundamental understanding and application of Ba0.5Sr0.5Co0.8Fe0.2O3−δ perovskite in energy storage and conversion: Past, present, and future. Energy Fuels 2021, 35, 13585–13609. [Google Scholar] [CrossRef]
  13. Liang, M.; Zhu, Y.; Song, Y.; Guan, D.; Luo, Z.; Yang, G.; Jiang, S.P.; Zhou, W.; Ran, R.; Shao, Z. A new durable surface nanoparticles-modified perovskite cathode for protonic ceramic fuel cells from selective cation exsolution under oxidizing atmosphere. Adv. Mater. 2021, 34, 2106379. [Google Scholar] [CrossRef]
  14. Yang, T.; Kollasch, S.L.; Grimes, J.; Xue, A.; Barnett, S.A. (La0.8Sr0.2)0.98MnO3−δ-Zr0.92Y0.16O2−δ: PrOx for oxygen electrode supported solid oxide cells. Appl. Catal. B Environ. 2022, 306, 121114. [Google Scholar] [CrossRef]
  15. Tong, X.; Ovtar, S.; Brodersen, K.; Hendriksen, P.V.; Chen, M. Large-area solid oxide cells with La0.6Sr0.4CoO3−δ infiltrated oxygen electrodes for electricity generation and hydrogen production. J. Power Sources 2020, 451, 227742. [Google Scholar] [CrossRef]
  16. Teng, Z.; Xiao, Z.; Yang, G.; Guo, L.; Yang, X.; Ran, R.; Wang, W.; Zhou, W.; Shao, Z. Efficient water splitting through solid oxide electrolysis cells with a new hydrogen electrode derived from A-site cation-deficient La0.4Sr0.55Co0.2Fe0.6Nb0.2O3−δ perovskite. Mater. Today Energy 2020, 17, 100458. [Google Scholar] [CrossRef]
  17. Wei, B.; Chen, K.; Zhao, L.; Lü, Z. Chromium deposition and poisoning at La0.6Sr0.4Co0.2Fe0.8O3−δ oxygen electrodes of solid oxide electrolysis cells. Phys. Chem. Chem. Phys. 2015, 17, 1601–1609. [Google Scholar] [CrossRef]
  18. Shao, Z.; Haile, S.M. A high-performance cathode for the next generation of solid-oxide fuel cells. Nature 2004, 431, 170–173. [Google Scholar] [CrossRef]
  19. Zhang, W.; Yu, B.; Xu, J. Investigation of single SOEC with BSCF anode and SDC barrier layer. Int. J. Hydrogen Energy 2012, 37, 837–842. [Google Scholar] [CrossRef]
  20. Duan, C.; Hook, D.; Chen, Y.; Tong, J.; O’Hayre, R. Zr and Y co-doped perovskite as a stable, high performance cathode for solid oxide fuel cells operating below 500 °C. Energy Environ. Sci. 2017, 10, 176–182. [Google Scholar] [CrossRef]
  21. Kuai, X.; Yang, G.; Chen, Y.; Sun, H.; Dai, J.; Song, Y.; Ran, R.; Wang, W.; Zhou, W.; Shao, Z. Boosting the activity of BaCo0.4Fe0.4Zr0.1Y0.1O3−δ perovskite for oxygen reduction reactions at low-to-intermediate temperatures through tuning B-site cation deficiency. Adv. Energy Mater. 2019, 9, 1902384. [Google Scholar] [CrossRef]
  22. Zhou, W.; Sunarso, J.; Zhao, M.; Liang, F.; Klande, T.; Feldhoff, A. A highly active perovskite electrode for the oxygen reduction reaction below 600 °C. Angew. Chem. Int. Ed. 2013, 52, 14036–14040. [Google Scholar] [CrossRef]
  23. Trini, M.; Hauch, A.; De Angelis, S.; Tong, X.; Hendriksen, P.V.; Chen, M. Comparison of microstructural evolution of fuel electrodes in solid oxide fuel cells and electrolysis cells. J. Power Sources 2020, 450, 227599. [Google Scholar] [CrossRef]
  24. Wang, Y.; Lei, X.; Zhang, Y.; Chen, F.; Liu, T. In-situ growth of metallic nanoparticles on perovskite parent as a hydrogen electrode for solid oxide cells. J. Power Sources 2018, 405, 114–123. [Google Scholar] [CrossRef]
  25. Yoon, K.J.; Lee, S.I.; An, H.; Kim, J.; Son, J.W.; Lee, J.H.; Je, H.J.; Lee, H.W.; Kim, B.K. Gas transport in hydrogen electrode of solid oxide regenerative fuel cells for power generation and hydrogen production. Int. J. Hydrogen Energy 2014, 39, 3868–3878. [Google Scholar] [CrossRef]
  26. Kim, J.; Jun, A.; Gwon, O.; Yoo, S.; Liu, M.; Shin, J.; Lim, T.H.; Kim, G. Hybrid-solid oxide electrolysis cell: A new strategy for efficient hydrogen production. Nano Energy 2018, 44, 121–126. [Google Scholar] [CrossRef]
  27. Chen, T.; Zhou, Y.; Liu, M.; Yuan, C.; Ye, X.; Zhan, Z.; Wang, S. High performance solid oxide electrolysis cell with impregnated electrodes. Electrochem. Commun. 2015, 54, 23–27. [Google Scholar] [CrossRef]
  28. Sun, W.; Zhang, N.; Mao, Y.; Sun, K. Preparation of dual-pore anode supported Sc2O3-stabilized-ZrO2 electrolyte planar solid oxide fuel cell by phase-inversion and dip-coating. J. Power Sources 2012, 218, 352–356. [Google Scholar] [CrossRef]
  29. Huang, H.; Lin, J.; Wang, Y.; Wang, S.; Xia, C.; Chen, C. Facile one-step forming of NiO and yttrium-stabilized zirconia composite anodes with straight open pores for planar solid oxide fuel cell using phase-inversion tape casting method. J. Power Sources 2015, 274, 1114–1117. [Google Scholar] [CrossRef]
  30. Liu, T.; Wang, Y.; Zhang, Y.; Fang, S.; Lei, L.; Ren, C.; Chen, F. Steam electrolysis in a solid oxide electrolysis cell fabricated by the phase-inversion tape casting method. Electrochem. Commun. 2015, 61, 106–109. [Google Scholar] [CrossRef]
  31. Gao, J.; Meng, Y.; Hong, T.; Kim, S.; Lee, S.; He, K.; Brinkman, K.S. Rational anode design for protonic ceramic fuel cells by a one-step phase inversion method. J. Power Sources 2019, 418, 162–166. [Google Scholar] [CrossRef]
  32. Gu, H.; Yang, G.; Hu, Y.; Liang, M.; Chen, S.; Ran, R.; Xu, M.; Wang, W.; Zhou, W.; Shao, Z. Enhancing the oxygen reduction activity of PrBaCo2O5+δ double perovskite cathode by tailoring the calcination temperatures. Int. J. Hydrogen Energy 2020, 45, 25996–26004. [Google Scholar] [CrossRef]
  33. Shi, H.; Zhou, W.; Ran, R.; Shao, Z. Comparative study of doped ceria thin-film electrolytes prepared by wet powder spraying with powder synthesized via two techniques. J. Power Sources 2010, 195, 393–401. [Google Scholar] [CrossRef]
  34. Suzuki, T.; Hasan, Z.; Funahashi, Y.; Yamaguchi, T.; Fujishiro, Y.; Awano, M. Impact of anode microstructure on solid oxide fuel cells. Science 2009, 325, 852–855. [Google Scholar] [CrossRef]
  35. Zheng, K.; Ni, M. Reconstruction of solid oxide fuel cell electrode microstructure and analysis of its effective conductivity. Sci. Bull. 2016, 61, 78–85. [Google Scholar] [CrossRef] [Green Version]
  36. Jin, C.; Yang, C.; Chen, F. Effects on microstructure of NiO–YSZ anode support fabricated by phase-inversion method. J. Membr. Sci. 2010, 363, 250–255. [Google Scholar] [CrossRef]
  37. Park, B.K.; Scipioni, R.; Barnett, S.A. Enhancement of Ni–(Y2O3)0.08(ZrO2)0.92 fuel electrode performance by infiltration of Ce0.8Gd0.2O2−δ nanoparticles. J. Mater. Chem. A 2020, 8, 4099–4106. [Google Scholar] [CrossRef]
  38. Qiao, J.; Zhang, N.; Wang, Z.; Mao, Y.; Sun, K.; Yuan, Y. Performance of mix-impregnated CeO2-Ni/YSZ anodes for direct oxidation of methane in solid oxide fuel cells. Fuel Cells 2009, 9, 729–739. [Google Scholar] [CrossRef]
  39. Zhang, Y.; Yang, G.; Chen, G.; Ran, R.; Zhou, W.; Shao, Z. Evaluation of the CO2 poisoning effect on a highly active cathode SrSc0.175Nb0.025Co0.8O3−δ in the oxygen reduction reaction. ACS Appl. Mater. Interfaces 2016, 8, 3003–3011. [Google Scholar] [CrossRef] [PubMed]
  40. Yan, A.; Liu, B.; Dong, Y.; Tian, Z.; Wang, D.; Cheng, M. A temperature programmed desorption investigation on the interaction of Ba0.5Sr0.5Co0.8Fe0.2O3−δ perovskite oxides with CO2 in the absence and presence of H2O and O2. Appl. Catal. B Environ. 2008, 80, 24–31. [Google Scholar] [CrossRef]
  41. Wang, J.; Yang, Z.; Ba, L.; Chen, Y.; Ge, B.; Peng, S. Effects of CO2 and H2O on Ba0.9Co0.7Fe0.2Nb0.1O3−δ cathode and modification by a Ce0.9Gd0.1O2−δ coating. J. Electroanal. Chem. 2018, 827, 79–84. [Google Scholar] [CrossRef]
  42. Chen, D.; Yang, G.; Ciucci, F.; Tadé, M.O.; Shao, Z. 3D core–shell architecture from infiltration and beneficial reactive sintering as highly efficient and thermally stable oxygen reduction electrode. J. Mater. Chem. A. 2014, 2, 1284–1293. [Google Scholar] [CrossRef]
  43. Duan, Z.; Yang, M.; Yan, A.; Hou, Z.; Dong, Y.; Chong, Y.; Chen, M.; Yang, W. Ba0.5Sr0.5Co0.8Fe0.2O3−δ as a cathode for IT-SOFCs with a GDC interlayer. J. Power Sources 2006, 160, 57–64. [Google Scholar] [CrossRef]
  44. Yoo, S.; Shin, J.Y.; Kim, G. Thermodynamic and electrical properties of layered perovskite NdBaCo2−xFexO5+δ−YSZ (x = 0, 1) composites for intermediate temperature SOFC cathodes. J. Electrochem. Soc. 2011, 158, B632–B638. [Google Scholar] [CrossRef]
  45. Thaheem, I.; Kim, K.J.; Lee, J.J.; Joh, D.W.; Jeong, I.; Lee, K.T. High performance Mn1.3Co1.3Cu0.4O4 spinel based composite cathodes for intermediate temperature solid oxide fuel cells. J. Mater.Chem. A 2019, 7, 19696–19703. [Google Scholar] [CrossRef]
  46. Tian, Y.; Liu, Y.; Wang, W.; Jia, L.; Pu, J.; Chi, B.; Li, J. High performance and stability of double perovskite-type oxide NdBa0.5Ca0.5Co1.5Fe0.5O5+δ as an oxygen electrode for reversible solid oxide electrochemical cell. J. Energy Chem. 2020, 43, 108–115. [Google Scholar] [CrossRef] [Green Version]
  47. Chen, Y.; Yoo, S.; Zhang, W.; Kim, J.H.; Zhou, Y.; Pei, K.; Kane, N.; Zhao, B.; Murphy, R.; Choi, Y.M.; et al. Effective promotion of oxygen reduction reaction by in situ formation of nanostructured catalyst. ACS Catal. 2019, 9, 7137–7142. [Google Scholar] [CrossRef]
  48. Tian, Y.; Li, J.; Liu, Y.; Yang, J.; Liu, B.; Jia, L.; Jiang, J.; Chi, B.; Pu, J.; Li, J. Preparation and properties of PrBa0.5Sr0.5Co1.5Fe0.5O5+δ as novel oxygen electrode for reversible solid oxide electrochemical cell. Int. J. Hydrogen Energy 2018, 43, 12603–12609. [Google Scholar] [CrossRef]
  49. López-Robledo, M.J.; Laguna-Bercero, M.A.; Larrea, A.; Orera, V.M. Reversible operation of microtubular solid oxide cells using La0.6Sr0.4Co0.2Fe0.8O3−δ-Ce0.9Gd0.1O2−δ oxygen electrodes. J. Power Sources 2018, 378, 184–189. [Google Scholar] [CrossRef] [Green Version]
  50. Kim, Y.D.; Yang, J.Y.; Saqib, M.; Park, K.; Shin, J.S.; Jo, M.; Park, K.M.; Lim, H.T.; Song, S.J.; Park, J.Y. Cobalt-free perovskite Ba1−xNdxFeO3−δ air electrode materials for reversible solid oxide cells. Ceram. Int. 2021, 47, 7985–7993. [Google Scholar] [CrossRef]
  51. Li, Y.; Tian, Y.; Li, J.; Pu, J.; Chi, B. Sr-free orthorhombic perovskite Pr0.8Ca0.2Fe0.8Co0.2O3−δ as a high-performance air electrode for reversible solid oxide cell. J. Power Sources 2022, 528, 231202. [Google Scholar] [CrossRef]
  52. Yun, B.H.; Kim, K.J.; Joh, D.W.; Chae, M.S.; Lee, J.J.; Kim, D.W.; Kang, D.; Choi, D.; Hong, S.t.; Lee, K.T. Highly active and durable double-doped bismuth oxide-based oxygen electrodes for reversible solid oxide cells at reduced temperatures. J. Mater. Chem. A 2019, 7, 20558–20566. [Google Scholar] [CrossRef]
  53. Khan, M.S.; Xu, X.; Knibbe, R.; Zhu, Z. Air electrodes and related degradation mechanisms in solid oxide electrolysis and reversible solid oxide cells. Renew. Sustain. Energy Rev. 2021, 143, 110918. [Google Scholar] [CrossRef]
  54. Heidari, D.; Javadpour, S.; Chan, S.H. Optimization of BSCF-SDC composite air electrode for intermediate temperature solid oxide electrolyzer cell. Energy Convers. Manag. 2017, 136, 78–84. [Google Scholar] [CrossRef]
  55. Chen, T.; Liu, M.; Yuan, C.; Zhou, Y.; Ye, X.; Zhan, Z.; Xia, C.; Wang, S. High performance of intermediate temperature solid oxide electrolysis cells using Nd2NiO4+δ impregnated scandia stabilized zirconia oxygen electrode. J. Power Sources 2015, 276, 1–6. [Google Scholar] [CrossRef]
  56. Laguna-Bercero, M.A.; Monzón, H.; Larrea, A.; Orera, V.M. Improved stability of reversible solid oxide cells with a nickelate-based oxygen electrode. J. Mater. Chem. A 2016, 4, 1446–1453. [Google Scholar] [CrossRef] [Green Version]
  57. 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]
  58. Matsui, T.; Kishida, R.; Kim, J.Y.; Muroyama, H.; Eguchi, K. Performance deterioration of Ni–YSZ anode induced by electrochemically generated steam in solid oxide fuel cells. J. Electrochem. Soc. 2000, 157, B776–B781. [Google Scholar] [CrossRef]
  59. Hubert, M.; Laurencin, J.; Cloetens, P.; Morel, B.; Montinaro, D.; Lefebvre-Joud, F. Impact of nickel agglomeration on solid oxide cell operated in fuel cell and electrolysis modes. J. Power Sources 2018, 397, 240–251. [Google Scholar] [CrossRef]
Molecules 27 08396 g001 550
Figure 1. Cross-sectional FE-SEM images of hydrogen electrodes produced by tape-casting (a,b) and phase-inversion tape-casting (c,d) after calcining at 1400 °C for 5 h (not reduced).
Figure 1. Cross-sectional FE-SEM images of hydrogen electrodes produced by tape-casting (a,b) and phase-inversion tape-casting (c,d) after calcining at 1400 °C for 5 h (not reduced).
Molecules 27 08396 g001
Molecules 27 08396 g002 550
Figure 2. The cross-sectional FE-SEM images of tape-casting (a,c,e), and phase-inversion tape-casting (b,d,f) hydrogen electrodes after the cell test (reduced).
Figure 2. The cross-sectional FE-SEM images of tape-casting (a,c,e), and phase-inversion tape-casting (b,d,f) hydrogen electrodes after the cell test (reduced).
Molecules 27 08396 g002
Molecules 27 08396 g003 550
Figure 3. Pore size distribution of tape-casting and phase-inversion tape-casting hydrogen electrodes calcined at 1350 °C after reduction under hydrogen atmosphere at 750 °C for 5 h.
Figure 3. Pore size distribution of tape-casting and phase-inversion tape-casting hydrogen electrodes calcined at 1350 °C after reduction under hydrogen atmosphere at 750 °C for 5 h.
Molecules 27 08396 g003
Molecules 27 08396 g004 550
Figure 4. (a) STEM image of the cross-section of the phase-inversion tape-casting hydrogen electrode after reduction in H2 at 750 °C for 5 h. Elemental mapping of Zr (b), Y (c), Ni (d), and O (e), and STEM-EDX result of Ni-YSZ (f).
Figure 4. (a) STEM image of the cross-section of the phase-inversion tape-casting hydrogen electrode after reduction in H2 at 750 °C for 5 h. Elemental mapping of Zr (b), Y (c), Ni (d), and O (e), and STEM-EDX result of Ni-YSZ (f).
Molecules 27 08396 g004
Molecules 27 08396 g005 550
Figure 5. XRD patterns of the oxygen electrodes before and after 10% H2O-Ar treatment at 750 °C for 5 h: (a) BSCF; (b) SSNC. ◆ Ba(OH)2 impurity.
Figure 5. XRD patterns of the oxygen electrodes before and after 10% H2O-Ar treatment at 750 °C for 5 h: (a) BSCF; (b) SSNC. ◆ Ba(OH)2 impurity.
Molecules 27 08396 g005
Molecules 27 08396 g006 550
Figure 6. FE-SEM images of the oxygen electrodes after 10% H2O-Ar treatment at 750 °C for 5 h: (a,b) SSNC; (c,d) BSCF.
Figure 6. FE-SEM images of the oxygen electrodes after 10% H2O-Ar treatment at 750 °C for 5 h: (a,b) SSNC; (c,d) BSCF.
Molecules 27 08396 g006
Molecules 27 08396 g007 550
Figure 7. I-V and I-P curves for the single cells measured at different temperatures. (a) Cell 1, (b) Cell 2, (c) Cell 3, and (d) a comparison of peak power densities of three cells at the operating temperatures.
Figure 7. I-V and I-P curves for the single cells measured at different temperatures. (a) Cell 1, (b) Cell 2, (c) Cell 3, and (d) a comparison of peak power densities of three cells at the operating temperatures.
Molecules 27 08396 g007
Molecules 27 08396 g008 550
Figure 8. Voltage versus current density measured at different temperatures in air and 50 vol.% H2-50 vol.% H2O. (a) Cell 1, (b) Cell 2, (c) Cell 3, and (d) comparison of the current densities at 1.3 V of the three cells at different temperatures.
Figure 8. Voltage versus current density measured at different temperatures in air and 50 vol.% H2-50 vol.% H2O. (a) Cell 1, (b) Cell 2, (c) Cell 3, and (d) comparison of the current densities at 1.3 V of the three cells at different temperatures.
Molecules 27 08396 g008
Molecules 27 08396 g009 550
Figure 9. The stability of Cell 2 operated between the electrolysis (@ −0.5 A cm−2) and fuel cell modes (@ 0.5 A cm−2) at 650 °C.
Figure 9. The stability of Cell 2 operated between the electrolysis (@ −0.5 A cm−2) and fuel cell modes (@ 0.5 A cm−2) at 650 °C.
Molecules 27 08396 g009
Table
Table 1. The various parameters of SOCs in this study.
Table 1. The various parameters of SOCs in this study.
Hydrogen ElectrodeElectrolyteOxygen Electrode
Cell 1Traditional tape castingYSZ-SDCSSNC
Cell 2Phase-inversion tape-castingYSZ-SDCSSNC
Cell 3Phase-inversion tape-castingYSZ-SDCBSCF
Table
Table 2. Comparison of the electrochemical performance of various SOFCs.
Table 2. Comparison of the electrochemical performance of various SOFCs.
Cell CompositionTemp. (°C)PPDs (W cm−2)Ref.
Ni-YSZ a|YSZ|SDC|SSNC7502.3This work
Ni-YSZ a|Ni-ScSZ b|ScSZ|LSM-ScSZ|LSM7501.32[28]
Ni-YSZ a|YSZ|LSM-YSZ8000.78[29]
Ni-YSZ-GDC c|GDC|YSZ|GDC|STFC d750~1.9[37]
Ni-YSZ|YSZ|SDC|SC-SDC e750~1.75[42]
Ni-YSZ|YSZ|GDC|BSCF8001.56[43]
Ni-YSZ|YSZ|NBCF f-YSZ8001.44[44]
Ni-YSZ|Ni-ScSZ|ScSZ|MCCO g-ScSZ8001.92[45]
Ni-YSZ|YSZ|GDC|NBCCF h-GDC8501.39[46]
Ni-YSZ|YSZ|SDC|BC-PBCC i750~1.15[47]
Ni-YSZ|YSZ|GDC|PBSCF j800~1.0[48]
Ni-YSZ|YSZ|GDC|GDC-LSCF|LSCF800~0.8[49]
Ni-YSZ|YSZ|SDC|SDC-BNF k8001.2[50]
Ni-YSZ|YSZ|GDC|PCFC l750~0.85[51]
a phase-inversion tape-casting method, b ScSZ: 10 mol% Sc2O3-ZrO2,c GDC: Ce0.9Gd0.1O2, d STFC: Sr(Ti0.3Fe0.63Co0.07)O3−δ, e SC-SDC: SrCoO3−δ impregnated into SDC, f NBCF: NdBaCoFeO5+δ, g MCCO: Mn1.3Co1.3Cu0.4O4, h NBCCF: NdBa0.5Ca0.5Co1.5Fe0.5O5+δ, i BC-PBCC: BaCoO3−δ-PrBa0.8Ca0.2Co2O5+δ, j PBSCF: PrBa0.5Sr0.5Co1.5Fe0.5O5+δ, k BNF: Ba0.97Nd0.03FeO3−δ, l PCFC: Pr0.8Ca0.2Fe0.8Co0.2O3−δ.
Table
Table 3. Comparison of the electrochemical performance of various SOECs for H2O electrolysis.
Table 3. Comparison of the electrochemical performance of various SOECs for H2O electrolysis.
Cell CompositionTemp. (°C)Gas Compositionj (A cm−2) at 1.3 VRef.
Ni-YSZ|YSZ|SDC|SSNC750H2/H2O (50/50)−1.59This work
Ni-YSZ a|YSZ|LSM-YSZ800H2/H2O (67/33)−1.35[30]
Ni-YSZ|YSZ|GDC|PBSCF750H2/H2O (70/30)−0.6[44]
Ni-YSZ|YSZ|GDC|NBCCF-GDC800H2/H2O (50/50)−0.92[46]
Ni-YSZ|YSZ|GDC|PBSCF800H2/H2O (50/50)−1.3[48]
Ni-YSZ|YSZ|GDC|GDC-LSCF|LSCF800H2/H2O (50/50)−0.85[49]
Ni-YSZ|YSZ|SDC|SDC-BNF800H2/H2O (50/50)−2.05[50]
Ni-YSZ|YSZ|GDC|PCFC750H2/H2O (50/50)−0.79[51]
Ni-YSZ|YSZ|SDC|BSCF-SDC800H2/H2O (50/50)−0.62[54]
Ni-YSZ|ScSZ|NNO b-ScSZ800H2/H2O (50/50)−1.08[55]
Ni-YSZ|YSZ|SDC|PNO c-GDC800H2/H2O (50/50)−0.78[56]
NiYSZ|YSZ|SDC|LSFCN d800H2/H2O (50/50)−1.04[57]
a phase-inversion tape-casting method, b NNO: Nd2NiO4+δ, c PNO: Pr2NiO4+δ, d LSCFN: La0.5Sr0.5Fe0.8Cu0.15Nb0.05O3−δ.
Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Share and Cite

MDPI and ACS Style

Yang, M.; Yang, C.; Liang, M.; Yang, G.; Ran, R.; Zhou, W.; Shao, Z. Solid Oxide Cells with Phase-Inversion Tape-Casted Hydrogen Electrode and SrSc0.175Nb0.025Co0.8O3−δ Oxygen Electrode for High-Performance Reversible Power Generation and Hydrogen Production. Molecules 2022, 27, 8396. https://doi.org/10.3390/molecules27238396

AMA Style

Yang M, Yang C, Liang M, Yang G, Ran R, Zhou W, Shao Z. Solid Oxide Cells with Phase-Inversion Tape-Casted Hydrogen Electrode and SrSc0.175Nb0.025Co0.8O3−δ Oxygen Electrode for High-Performance Reversible Power Generation and Hydrogen Production. Molecules. 2022; 27(23):8396. https://doi.org/10.3390/molecules27238396

Chicago/Turabian Style

Yang, Meiting, Changjiang Yang, Mingzhuang Liang, Guangming Yang, Ran Ran, Wei Zhou, and Zongping Shao. 2022. "Solid Oxide Cells with Phase-Inversion Tape-Casted Hydrogen Electrode and SrSc0.175Nb0.025Co0.8O3−δ Oxygen Electrode for High-Performance Reversible Power Generation and Hydrogen Production" Molecules 27, no. 23: 8396. https://doi.org/10.3390/molecules27238396

Article Metrics

Back to TopTop