Yb2O3 Doped Zr0.92Y0.08O2-α(8YSZ) and Its Composite Electrolyte for Intermediate Temperature Solid Oxide Fuel Cells

Yb3+ and Y3+ double doped ZrO2 (8YSZ+4Yb2O3) samples were synthesized by a solid state reaction method. Moreover, 8YSZ+4Yb2O3-NaCl/KCl composites were also successfully produced at different temperatures. The 8YSZ+4Yb2O3, 8YSZ+4Yb2O3-NaCl/KCl (800 °C), and 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) samples were characterized by x–ray diffraction (XRD) and scanning electron microscopy (SEM). The results showed that a dense composite electrolyte was formed at a low temperature of 800 °C. The maximum conductivities of 4.7 × 10−2 S·cm−1, 6.1 × 10−1 S·cm−1, and 3.8 × 10−1 S·cm−1 were achieved for the 8YSZ+4Yb2O3, 8YSZ+4Yb2O3-NaCl/KCl (800 °C), and 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) samples at 700 °C, respectively. The logσ~log (pO2) plot result showed that the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite electrolyte is a virtually pure ionic conductor. An excellent performance of the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite was obtained with a maximum power density of 364 mW·cm−2 at 700 °C.

Composite electrolyte materials, which have high conductivities, are pivotal to the development of intermediate temperature fuel cells. In recent years, two-phase composite electrolytes consisting of doped BaCeO 3 , SrCeO 3 , CeO 2 , chloride, and carbonate have exhibited enhanced ionic conductivities and intermediate temperature fuel cell performance [18][19][20][21][22][23][24]. For example, Park et al. combined a perovskite-type BaCeO 3 based electrolyte with a binary eutectic carbonate to obtain a high ionic conductivity of 0.176 S·cm −1 at 550 • C [18]. Fu et al. studied a gadolinium-doped ceria chloride composite electrolyte with a good power output density of 240 mW·cm −2 at 500 • C [24].
Many studies have shown that double cation doped ZrO 2 could reduce the test temperature and improve its conductivity when compared to the single cation stabilized zirconia [25][26][27][28][29][30]. For instance,  [26]. Wang et al. stabilized the structure phase when the substitution of Yb 2 O 3 was over 2 mol % in the Yb 2 O 3 -Sc 2 O 3 -ZrO 2 system. Furthermore, the radius of Yb 3+ and Y 3+ were both close to that of Zr 4+ [27]. Therefore, we tried to fabricate a new composite electrolyte by using Yb 3+ and Y 3+ double doped ZrO 2 together with a binary eutectic chloride. In this paper, new Yb 2 O 3 doped Zr 0.92 Y 0.08 O 2-α (8YSZ)-NaCl/KCl composite electrolytes were prepared at different temperatures. The morphology and structure were characterized and the ionic conductivity and fuel cell were systematically evaluated.

Experimental
Yb 3+ and Y 3+ double doped ZrO 2 was produced via a solid state reaction method. A total of 4 mol % Yb 2 O 3 (99.9%) and 8YSZ (Xuancheng Jingrui New Material Co., Ltd., Xuancheng, China, sol-gel method, 50 nm) powders were fully mixed in ethanol under continuous stirring with an agate mortar and dried by an infrared lamp three times. Subsequently, the obtained powder was calcined at 1200 • C for 6 h to obtain the 8YSZ and 8YSZ+4Yb 2 O 3 samples.
All samples were ground and pressed into thin slices (thickness = 1.0-1.2 mm) and 80% silver-20% palladium paste (areas = 0.5 cm 2 ) was used with silver wires as the electrodes. Electrochemical impedance spectroscopy (EIS) techniques were used to obtain the conductivity of the 8YSZ+4Yb 2 O 3 , 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C), and 8YSZ+4Yb 2 O 3 -NaCl/KCl (1000 • C). The ac amplitude was 20 mV in a three-electrode system over the frequency range from 1 Hz to 1 MHz. The conductivity can be calculated from: σ = L R·S , where σ is conductivity, L is thickness, R is resistance, and S is the surface area of the electrolyte pellet [32,33]. The effects of different synthetic temperature, operating temperature, and oxygen partial pressure on the electrical conductivities were determined with an electrochemical analyzer (CHI660E, Chen Hua company, Shanghai, China) at 400-700 • C [34,35]. Oxygen concentration discharge cell: air, Pd-Ag|8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C)|Pd-Ag, O 2 at 700 • C and H 2 /O 2 fuel cells using 8YSZ+4Yb 2 O 3 and 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) as electrolytes (thickness = 1.1 mm) were constructed. The fuel cell was tested by using the linear scanning of current and voltage method within the CHI660E electrochemical analyzer [33]. The 8YSZ (Xuancheng Jingrui New Material Co., Ltd., sol-gel method, 50 nm) powder possessed coexisting tetragonal and monoclinic phases, where the tetragonal was the major phase, as shown in Figure 1a. When the synthesis temperature reached 1200 • C, it was observed that the 8YSZ and 8YSZ+4Yb 2 O 3 showed an entire t-ZrO 2 phase. Yb 3+ really formed a solid solution with YSZ and there was no trace of Yb 2 O 3 . Additionally, NaCl and KCl diffraction peaks also existed in the 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) and 8YSZ+4Yb 2 O 3 -NaCl/KCl (1000 • C) samples, that is to say that the binary eutectic chloride did not react with 8YSZ+4Yb 2 O 3 . This was in good agreement with the studies of ceria-carbonates or doped SrCeO 3 -NaCl-KCl composite electrolytes [36,37].

Results and Discussion
with YSZ and there was no trace of Yb2O3. Additionally, NaCl and KCl diffraction peaks also existed in the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) and 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) samples, that is to say that the binary eutectic chloride did not react with 8YSZ+4Yb2O3. This was in good agreement with the studies of ceria-carbonates or doped SrCeO3-NaCl-KCl composite electrolytes [36,37].  The surface (a,c,e) and cross-sectional (b,d,f) morphologies of the 8YSZ+4Yb2O3, 8YSZ+4Yb2O3-NaCl/KCl (800 °C) ,and 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) pellets, as seen using SEM, are exhibited in Figure 2. No pores or cracks on the surface (e) and cross-sectional (f) photos of the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) were seen along the entire experiment, which meant that the Yb 3+ and Y 3+ double doped ZrO2 and the binary eutectic chloride sintered uniformly. The 8YSZ+4Yb2O3 and NaCl/KCl are indicated by arrows in Figure 2f. However, as can be observed from Figures 2c,d, a few scattered small pores were found in the 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) pellet, which may influence the electrical properties of the sample. The sintering performance of the 8YSZ+4Yb2O3-NaCl/KCl pellet increased with the increase in temperature, nevertheless, the vapor pressure of the molten inorganic salts rapidly increased at the same time. This was consistent with the ceria-carbonates or doped SrCeO3-chloride composite electrolytes prepared under similar heat treatments [36][37][38][39]. Therefore, the most suitable synthetic temperature was 800 °C.
The plots of log (σT) versus 1000 T −1 of the 8YSZ, 8YSZ+4Yb2O3, 8YSZ+4Yb2O3-NaCl/KCl (800 °C), and 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) pellets in air at 400-700 °C are given in Figure 3. The The surface (a,c,e) and cross-sectional (b,d,f) morphologies of the 8YSZ+4Yb 2 O 3 , 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) ,and 8YSZ+4Yb 2 O 3 -NaCl/KCl (1000 • C) pellets, as seen using SEM, are exhibited in Figure 2. No pores or cracks on the surface (e) and cross-sectional (f) photos of the 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) were seen along the entire experiment, which meant that the Yb 3+ and Y 3+ double doped ZrO 2 and the binary eutectic chloride sintered uniformly. The 8YSZ+4Yb 2 O 3 and NaCl/KCl are indicated by arrows in Figure 2f. However, as can be observed from Figure 2c,d, a few scattered small pores were found in the 8YSZ+4Yb 2 O 3 -NaCl/KCl (1000 • C) pellet, which may influence the electrical properties of the sample. The sintering performance of the 8YSZ+4Yb 2 O 3 -NaCl/KCl pellet increased with the increase in temperature, nevertheless, the vapor pressure of the molten inorganic salts rapidly increased at the same time. This was consistent with the ceria-carbonates or doped SrCeO 3 -chloride composite electrolytes prepared under similar heat treatments [36][37][38][39]. Therefore, the most suitable synthetic temperature was 800 • C.
Materials 2018, 11, x FOR PEER REVIEW 4 of 9 maximum conductivities achieved for 8YSZ+4Yb2O3, 8YSZ+4Yb2O3-NaCl/KCl (800 °C), and 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) were 4.7 × 10 −2 S·cm −1 , 6.1 × 10 −1 S·cm −1 , and 3.8 × 10 −1 S·cm −1 at 700 °C, respectively. Wang et al. [27] demonstrated that the conductivities of Yb 3+ and Sc 3+ double doped ZrO2 could maintain 1.0 × 10 −2 S·cm −1 at 700 °C, which is the threshold value for application as an electrolyte. The experimental result of Bohnke et al. [28] showed that the conductivity of the (Sc2O3)0.07-(Fe2O3)0.03-(ZrO2)0.90 was lower than 1.0 × 10 −2 S·cm −1 at 700 °C. Our result was equivalent to the former. The conductivities of electrolytes have been generally found to be higher in a wet atmosphere in comparison with a dry atmosphere [33]. Furthermore, 8YSZ+4Yb2O3 exhibited a highest electrical conductivity of 4.7 × 10 −2 S·cm −1 when compared to the 8YSZ of 2.3 × 10 −2 S·cm −1 at 700 °C. The measured conductivities of the composite electrolytes were much higher than those of 8YSZ+4Yb2O3 and in our previous study of SrCe0.9Sm0.1O3-α-NaCl-KCl (1.43 × 10 −1 S . cm −1 ). This revealed that the introduction of the binary eutectic chloride allows for ionic charge carriers to move quickly and freely through it, which is beneficial for the long-range transfer ability of ions [36,40]. In Figure 3, with the increase in sintering temperature, the conductivities of the 8YSZ+4Yb2O3-NaCl/KCl samples decreased. The conductivity of 8YSZ+4Yb2O3-NaCl/KCl (1000 °C) was lower than that of the sample sintered at 800 °C, especially at a low temperature range. This might be associated with the breaking of the long-range transfer of ionic charge carriers to a certain extent after heating at 1000 °C, according to the result of Figure 2.  To reveal the ionic conduction of the 8YSZ+4Yb2O3 and 8YSZ+4Yb2O3-NaCl/KCl (800 °C) samples, the variation of the conductivities with the partial pressures of oxygen in the range of pO2 = 10 −20~1 atm were evaluated. It can be seen from Figure 4 that the conductivities were almost independent of pO2 at 700 °C, implying that the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite electrolyte is a virtually pure ionic conductor, which agrees with previous reports [20,37,38]. The result illustrates that the conductivities of the two electrolytes in Figure 3 are purely ionic. To explore the oxide ionic conduction of the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite under an oxygen-containing atmosphere, an oxygen concentration discharge cell was fabricated and tested at 700 °C, as illustrated in Figure 5.  To reveal the ionic conduction of the 8YSZ+4Yb 2 O 3 and 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) samples, the variation of the conductivities with the partial pressures of oxygen in the range of pO 2 = 10 −20~1 atm were evaluated. It can be seen from Figure 4 that the conductivities were almost independent of pO 2 at 700 • C, implying that the 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) composite electrolyte is a virtually pure ionic conductor, which agrees with previous reports [20,37,38]. The result illustrates that the conductivities of the two electrolytes in Figure 3 are purely ionic. To reveal the ionic conduction of the 8YSZ+4Yb2O3 and 8YSZ+4Yb2O3-NaCl/KCl (800 °C) samples, the variation of the conductivities with the partial pressures of oxygen in the range of pO2 = 10 −20~1 atm were evaluated. It can be seen from Figure 4 that the conductivities were almost independent of pO2 at 700 °C, implying that the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite electrolyte is a virtually pure ionic conductor, which agrees with previous reports [20,37,38]. The result illustrates that the conductivities of the two electrolytes in Figure 3 are purely ionic. To explore the oxide ionic conduction of the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite under an oxygen-containing atmosphere, an oxygen concentration discharge cell was fabricated and tested at 700 °C, as illustrated in Figure 5.  believed to be an oxide ionic conductor under an oxygen-containing atmosphere due to the exhibited stable discharge curve [41,42]. composite was believed to be an oxide ionic conductor under an oxygen-containing atmosphere due to the exhibited stable discharge curve [41,42].  Figure 6 is the typical impedance spectra of the 8YSZ+4Yb2O3 and 8YSZ+4Yb2O3-NaCl/KCl (800 °C) measured at 700 °C under open-circuit conditions. The spectra gave an incomplete semicircle at intermediate to high frequencies, and an arc at low frequency. The high frequency related to the ohmic resistance (Ro) and the low frequency can be attributed to the resistance between the electrode and the electrolyte [43]. The interval between the high and low frequencies corresponded to interfacial polarization resistance (Rp) where the Rp and Ro of 8YSZ+4Yb2O3 were 0.41 Ω·cm 2 and 5.45 Ω·cm 2 , while those of 8YSZ+4Yb2O3-NaCl/KCl (800 °C) were 0.16 Ω·cm 2 and 0.87 Ω·cm 2 at 700 °C, correspondingly. The single cells based on 8YSZ+4Yb2O3 and 8YSZ+4Yb2O3-NaCl/KCl (800 °C) were operated at 700 °C, hydrogen and oxygen were supplied at the anode side and cathode side, respectively, and the I-V and power density curves are displayed in Figure 7. The following two reactions occur at the cathode and anode compartments: cathode reaction: 2H + + O2 + 4e − = H2O + O 2− and anode reaction: 2H2 + O 2− = 2H + + H2O + 4e − [44]. As can be observed from Figure 7, the open circuit voltages were as high as 1.09 V, which confirmed that the samples possessed high densities. This can be attributed to the fact that NaCl-KCl eutectic melt fills the pores inside the composite electrolyte, leading to the increase in the density of the composite electrolyte at 700 °C. In this state, the 8YSZ+4Yb2O3 The oxygen concentration discharge cell: air, Pd-Ag|8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C)|Pd-Ag, O 2 at 700 • C. Figure 6 is the typical impedance spectra of the 8YSZ+4Yb 2 O 3 and 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) measured at 700 • C under open-circuit conditions. The spectra gave an incomplete semicircle at intermediate to high frequencies, and an arc at low frequency. The high frequency related to the ohmic resistance (R o ) and the low frequency can be attributed to the resistance between the electrode and the electrolyte [43]. The interval between the high and low frequencies corresponded to interfacial polarization resistance (R p ) where the R p and R o of 8YSZ+4Yb 2 O 3 were 0.41 Ω·cm 2 and 5.45 Ω·cm 2 , while those of 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) were 0.16 Ω·cm 2 and 0.87 Ω·cm 2 at 700 • C, correspondingly. composite was believed to be an oxide ionic conductor under an oxygen-containing atmosphere due to the exhibited stable discharge curve [41,42].  Figure 6 is the typical impedance spectra of the 8YSZ+4Yb2O3 and 8YSZ+4Yb2O3-NaCl/KCl (800 °C) measured at 700 °C under open-circuit conditions. The spectra gave an incomplete semicircle at intermediate to high frequencies, and an arc at low frequency. The high frequency related to the ohmic resistance (Ro) and the low frequency can be attributed to the resistance between the electrode and the electrolyte [43]. The interval between the high and low frequencies corresponded to interfacial polarization resistance (Rp) where the Rp and Ro of 8YSZ+4Yb2O3 were 0.41 Ω·cm 2 and 5.45 Ω·cm 2 , while those of 8YSZ+4Yb2O3-NaCl/KCl (800 °C) were 0.16 Ω·cm 2 and 0.87 Ω·cm 2 at 700 °C, correspondingly. The single cells based on 8YSZ+4Yb2O3 and 8YSZ+4Yb2O3-NaCl/KCl (800 °C) were operated at 700 °C, hydrogen and oxygen were supplied at the anode side and cathode side, respectively, and the I-V and power density curves are displayed in Figure 7. The following two reactions occur at the cathode and anode compartments: cathode reaction: 2H + + O2 + 4e − = H2O + O 2− and anode reaction: 2H2 + O 2− = 2H + + H2O + 4e − [44]. As can be observed from Figure 7, the open circuit voltages were as high as 1.09 V, which confirmed that the samples possessed high densities. This can be attributed to the fact that NaCl-KCl eutectic melt fills the pores inside the composite electrolyte, leading to the increase in the density of the composite electrolyte at 700 °C. In this state, the 8YSZ+4Yb2O3 The single cells based on 8YSZ+4Yb 2 O 3 and 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) were operated at 700 • C, hydrogen and oxygen were supplied at the anode side and cathode side, respectively, and the I-V and power density curves are displayed in Figure 7. The following two reactions occur at the cathode and anode compartments: cathode reaction: 2H + + O 2 + 4e − = H 2 O + O 2− and anode reaction: 2H 2 + O 2− = 2H + + H 2 O + 4e − [44]. As can be observed from Figure 7, the open circuit voltages were as high as 1.09 V, which confirmed that the samples possessed high densities. This can be attributed to the fact that NaCl-KCl eutectic melt fills the pores inside the composite electrolyte, leading to the increase in the density of the composite electrolyte at 700 • C. In this state, the 8YSZ+4Yb 2 O 3 electrolyte and NaCl/KCl were between the continuous and discontinuous phases. The conductivities can be ascribed to the mobility of various species (Na + , K + , H + , Cl − and O 2− ). And protons vacancies are the predominated defects under wet conditions, especially in a hydrogen containing atmosphere. Therefore, the fuel cell based on 8YSZ+4Yb 2 O 3 -NaCl/KCl (800 • C) exhibited good cell performance and gave a power output density of 364 mW·cm −2 at 700 • C. The result was much better than the best performance of 8YSZ+4Yb 2 O 3 and that ever reported for intermediate temperature SOFCs based on SrCe 0.9 Eu 0.1 O 3-α -NaCl-KCl of 207 mW·cm −2 [37] at 700 • C. However, the durabilities of the electrolytes were not been tested, and will be done in future work.
Materials 2018, 11, x FOR PEER REVIEW 7 of 9 electrolyte and NaCl/KCl were between the continuous and discontinuous phases. The conductivities can be ascribed to the mobility of various species (Na + , K + , H + , Cl − and O 2− ). And protons vacancies are the predominated defects under wet conditions, especially in a hydrogen containing atmosphere. Therefore, the fuel cell based on 8YSZ+4Yb2O3-NaCl/KCl (800 °C) exhibited good cell performance and gave a power output density of 364 mW·cm −2 at 700 °C. The result was much better than the best performance of 8YSZ+4Yb2O3 and that ever reported for intermediate temperature SOFCs based on SrCe0.9Eu0.1O3-α-NaCl-KCl of 207 mW·cm −2 [37] at 700 °C. However, the durabilities of the electrolytes were not been tested, and will be done in future work.

Conclusions
In this study, Yb 3+ and Y 3+ double doped ZrO2 and its composite electrolytes were successfully fabricated by a solid state reaction method. The result of the logσ~log (pO2) plot indicated that the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite electrolyte was a virtually pure ionic conductor. Furthermore, the oxygen concentration discharge cell illustrated that the 8YSZ+4Yb2O3-NaCl/KCl (800 °C) composite was an oxide ionic conductor under an oxygen-containing atmosphere. The Rp and Ro were 0.41 Ω·cm 2 and 5.45 Ω·cm 2 for 8YSZ+4Yb2O3, and 0.16 Ω·cm 2 , and 0.87 Ω·cm 2 for 8YSZ+4Yb2O3-NaCl/KCl (800 °C) under open-circuit conditions at 700 °C correspondingly. Finally, an excellent performance of 8YSZ+4Yb2O3-NaCl/KCl (800 °C) was obtained with a maximum power density of 364 mW·cm −2 at 700 °C.