Improvement of La0.8Sr0.2MnO3−δ Cathode Material for Solid Oxide Fuel Cells by Addition of YFe0.5Co0.5O3

The high efficiency of solid oxide fuel cells with La0.8Sr0.2MnO3−δ (LSM) cathodes working in the range of 800–1000 °C, rapidly decreases below 800 °C. The goal of this study is to improve the properties of LSM cathodes working in the range of 500–800 °C by the addition of YFe0.5Co0.5O3 (YFC). Monophasic YFC is synthesized and sintered at 950 °C. Composite cathodes are prepared on Ce0.8Sm0.2O1.9 electrolyte disks using pastes containing YFC and LSM powders mixed in 0:1, 1:19, and 1:1 weight ratios denoted LSM, LSM1, and LSM1, respectively. X-ray diffraction patterns of tested composites reveal the presence of pure perovskite phases in samples sintered at 950 °C and the presence of Sr4Fe4O11, YMnO3, and La0.775Sr0.225MnO3.047 phases in samples sintered at 1100 °C. Electrochemical impedance spectroscopy reveals that polarization resistance increases from LSM1, by LSM, to LSM2. Differences in polarization resistance increase with decreasing operating temperatures because activation energy rises in the same order and equals to 1.33, 1.34, and 1.58 eV for LSM1, LSM, and LSM2, respectively. The lower polarization resistance of LSM1 electrodes is caused by the lower resistance associated with the charge transfer process.


Introduction
The slow kinetics of oxygen reduction reaction (ORR) on a cathode is the decisive factor for energy losses in solid oxide fuel cells (SOFCs). La 1−x Sr x MnO 3−δ (LSM) was the most frequently used cathode material for SOFC since 1973 [1]. LSM cathodes are effective in ORR at high temperatures (HT) (800-1000 • C) [2]. However, the rapid degradation of cells operating in the HT range prompted researchers to search for cathode materials suitable for SOFCs operating in the 500-800 • C range. In this range, cobalt-containing mixed oxides of the perovskite structure such as La 1−x Sr x CoO 3−δ , (LSC), Ba 1−x Sr x Co 1−y Fe y O 3−δ (BSCF), and La 1−x Sr x Co 1−y Fe y O 3−δ (LSCF) reveal superior ionic conductivity compared to LSM. LSCF is an often-used cathode material for comparison in papers reporting new cathode materials working in the IT range. Recently, layered double perovskites are intensively studied due to excellent ORR kinetics [3,4]. Although many new cathode materials have been developed [2,[5][6][7][8][9], improvement of physicochemical properties and electrochemical performance of the LSM material remains an urgent task.
LSM reveals excellent mechanical strength, electronic conductivity of 190 S cm −1 at 650 • C [10] and 230 S cm −1 at 900 • C [11], and a thermal expansion coefficient (TEC) equal to 11.1 × 10 −6 K −1 [6] in the range 300-1270 K, which makes it compatible with frequently used electrolyte materials [12]. These are the main reasons that cause LSM to be more attractive than compared to any other cathode material. It allows quick warm ups and cool downs the cell without degrading the cathode material, providing high operation stability and low susceptibility to failures caused by thermal shocks. Unlike almost all other cathode materials, there is no need to constantly keep LSM-based cells in the operating temperature at off-peak hours, saving its working resource and decreasing operational cost. LSM in reversible solid oxide cells reveals redox instability above 850 • C, whereas below 800 • C it is stable in both oxidizing and reducing atmospheres [13]. The main drawbacks of LSM are its insufficient ionic conductivity in oxidizing atmospheres [11] and a decrease in efficiency in lower temperatures [14]. The performance of LSM cathodes can be improved by an admixture of other cation(s) or by preparing composite electrodes with the addition of a second active phase. Yang et al. [15] prepared LSM-based cathodes in which La was partially replaced by Sr, Nd, Pr, and Sm and demonstrated its stability at 700 • C during 100-hour tests.
The improvement in the electrochemical performance of LSM with YSZ addition is caused by spatial enlargement of the triple-phase boundary area, increasing the number of electrochemically active sites for charge transfer reaction and oxygen adsorption [16]. Lee et al. [17] found that dissociative adsorption is the main rate-determining step of the ORR of LSM-YSZ composites and found that the best performances exhibit cathodes sintered at 1100 • C. Murray and Barnett [23] described LSM-GDC composite electrodes with a low-current interfacial resistance two to three times lower than LSM-YSZ composite ones. Other doped cerias such as Ce 0.8 Ln 0.2 O 2−δ (Ln = Gd, Er, Tb and Pr) and CoO x were added to LSM by Navarrete et al. [35]. The authors found that Pr Ce 0.8 Pr 0.2 O 2−δ exhibits the best electrochemical performance. Pajot et al. [26] optimized the strontium content in LSM/Bi 1.5 Er 0.5 O 3 -composite electrodes. These authors showed that these cathodes have R p of 0.1 and 3 Ω cm 2 at 675 and 500 • C, respectively. Strandbakke et al. [28] reported that composite cathodes LSM with lanthanum tungstate and platinum reveal polarization resistance 40 Ω cm 2 at 650 • C. Rehman et al. [18] described the properties of ternary composite LSM-YSZ-GDC, reporting maximum power densities of 215, 316, and 396 mW cm −2 at 750, 800, and 850 • C, respectively. Wang et al. [24] applied LSM-SDC composite cathode in low-temperature SOFC. The authors reported that the optimum ratio of LSM:SDC is 1:2. LT-SOFC with this material reached a power density of 742 mW cm −2 under 550 • C. The enhanced catalytic activities of LSM cathode-infiltrated metallic (Ag), ceramic LSF and CeO 2 nanocatalysts were reported by Seyed-Vakili et al. [31]. The authors found that the co-infiltration of Ag and ceria reduced the polarization resistance of the electrode to 2.5% of that for the pure LSM electrode. Furthermore, the infiltration of Ag solution reduced electrode overpotential by about 114% at 700 • C. Li et al. [36] assembled Co 3 O 4 catalysts on the LSM cathode's surface by using a hydrothermal method. The polarization resistance of the symmetric cell with the LSM cathode and modified LSM cathode was 0.95 Ω cm 2 and 0.55 Ω cm 2 at 700 • C, respectively. Shahrokhi et al. [33] infiltrated LSM oxygen electrodes with nanoparticles of La 2 Ni 0.5 Co 0.5 O 4 of the Ruddlesden-Popper structure and LaNi 0.5 Co 0.5 O 3 of the perovskite structure and found that La 2 Ni 0.5 Co 0.5 O 4 has greater impact than LaNi 0.5 Co 0.5 O 3 on both the decrease in polarization resistance and stability of the electrode under cyclic solid oxide electrolysis cell (SOEC) and SOFC modes. Liu et al. [14] tested LSM-LSCF composite cathodes. The authors found that a cell with an LSM-infiltrated LSCF cathode revealed at 825 • C a peak power density of 1.07 W cm −2 , about 24% higher than that of the same cell without LSM infiltration. LSM was studied as an electrode material for SOFC operating reversibly as SOECs [2,39], which are promising for the storage and regeneration of sustainable energy from solar and wind power energy sources. Zheng et al. [40] studied La 0.8 Sr 0.2 Co 0.8 Ni 0.2 O 3−δ -impregnated LSM-GDC composites, including oxygen electrodes. The authors reported a peak power density of 1057 mW cm −2 at 800 • C in the SOFC mode. In co-electrolysis modes, the current density reached 1.60 A cm −2 at 1.5 V at 800 • C with an H 2 O/CO 2 ratio of 2/1. Yu et al. [38] infiltrated FeO x nanoparticles onto an LSM backbone cathode. The infiltration process resulted in an increase of 3.4% in cell performance. LSM is also frequently used as a current collector layer [41] or a protective layer on a stainless-steel current collector.
Currently, mixed oxides of perovskite structure of the general formula ABO 3 are widely used in SOFC applications. Among them, YFe 0.5 Co 0.5 O 3 (YFC) reveals a polarization resistance of 0.07 Ω cm 2 at 750 • C, TEC of 17.5 × 10 −6 K −1 , and conductivity of 183 S cm −1 [42]. The excellent properties of YFC as a cathode material make it a promising candidate for implementation in the composite cathode for SOFCs. However, according to our knowledge, no other attempt has been made to develop the YFC-containing composite cathodes for SOFC application.
Porosity performs an essential function in enhancing the performance of SOFC electrodes because gas-phase diffusion resistance can be significant, even far away from the limiting current [43]. Controlling porosity can improve electrode performance by facilitating gas diffusion [44]. Laguna-Bercero et al. [45] reported microbeads with 6 µm diameter is a good pore former for generating a microstructure that works well in both SOEC and SOFC modes.
This study aims to improve the properties of LSM cathodes working in the range of 500-800 • C by the adding YFe 0.5 Co 0.5 O 3 . In order to precisely determine which parameters of the electrode process are affected by a given additive, all tests were carried out by using LSM without the addition of electrolyte materials (YSZ and GDC). The current collector layer has a huge impact on cathode efficiency [46,47]; therefore, such a layer was not used in the described experiments.

Synthesis of YFC Powder
YFC was synthesized by using the citric acid method. At first, Y 2 O 3 (supplied by Onyxmet, Olsztyn, Poland) was dissolved in nitric acid (Sigma-Aldrich, Saint Louis, USA, reagent grade) to obtain a transparent solution containing yttrium cations. Then, cobalt and iron nitrates (supplied by Sigma-Aldrich, Saint Louis, USA, reagent grade) in stoichiometric amounts (Y:Fe:Co = 1:0.5:0.5) were added. The obtained solution was continuously stirred with added dropwise citric acid under heating at 80 • C until the gel was obtained. The gel was dried at 110 • C to obtain bottle-green xerogel and then sintered at 950 • C for 10 h or 1100 • C for 10 h, as described in more detail in [42].

Characterization
In order to identify the crystalline phases formed after sintering LSM/YFC mixtures at different temperatures, X-ray diffraction patterns were collected in the 2θ range of 2-72 • with the use of an X'Pert PRO (PANalytical B.V., Cambridge, UK) diffractometer operated at 40 kV and 30 mA by applying Ni-filtered Cu K α radiation. Before measurements, the samples were uploaded on a silicon low-background sample holder. A Field Emission Scanning Electron Microscope JEOL JSM-7500F (JEOL Ltd. Tokyo, Japan) equipped with the RBEI retractable backscattered electron detector and INCA PentaFetx3 EDS detection system of characteristic X-ray radiation [48] was applied for imaging the morphology of the obtained composite cathodes. The porosity and BET-specific surface area of the samples were determined at 196 • C from nitrogen adsorption-desorption isotherms with the use of a Quantachrome Nova 2000 apparatus (Quantachrome Instruments, Boynton Beach, FL, USA) after outgassing for 3 h at 200 • C under vacuum.
The round working and reference electrodes of 5 mm in diameter were printed on 1-millimeter-thick SDC electrolyte half disks of 20 mm in diameter, prepared as described in [49] and covered by LSCF at the opposite side [49]. Then, cells were sintered at 950 • C or 1100 • C for 2 h ( Figure 1). A Field Emission Scanning Electron Microscope JEOL JSM-7500F (JEOL Ltd. Tokyo, Japan) equipped with the RBEI retractable backscattered electron detector and INCA Pen-taFetx3 EDS detection system of characteristic X-ray radiation [48] was applied for imaging the morphology of the obtained composite cathodes. The porosity and BET-specific surface area of the samples were determined at 196 °C from nitrogen adsorption-desorption isotherms with the use of a Quantachrome Nova 2000 apparatus (Quantachrome Instruments, Boynton Beach, FL, USA) after outgassing for 3 h at 200 °C under vacuum.
The round working and reference electrodes of 5 mm in diameter were printed on 1millimeter-thick SDC electrolyte half disks of 20 mm in diameter, prepared as described in [49] and covered by LSCF at the opposite side [49]. Then, cells were sintered at 950 °C or 1100 °C for 2 h (Figure 1).

The electrochemical Properties
The electrochemical properties of all electrodes were tested by using a Gamry 300 series potentiostat/galvanostat/ZRA (Gamry Instruments, Warminster, PA, USA) in gas mixtures of set oxygen partial pressures from 0.001 to 1 containing oxygen (99.

The Electrochemical Properties
The electrochemical properties of all electrodes were tested by using a Gamry 300 series potentiostat/galvanostat/ZRA (Gamry Instruments, Warminster, PA, USA) in gas mixtures of set oxygen partial pressures from 0.001 to 1 containing oxygen (99.5%, Air Liquide Polska Sp. z o. o., Kraków, Polska) or oxygen and argon (99.999%, Air Liquide Polska Sp. z o. o., Kraków, Polska) with a gas flow rate of 150 cm 3 min −1 . The cell was mounted in the alumina test fixture for electrochemical measurements as reported elsewhere [50]. Electrochemical impedance spectroscopy (EIS) spectra were recorded in a frequency range from 8 mHz to 300 kHz with a density of 8 frequency points per decade with AC voltage signal of 5 or 20 mV rms. Data treatment based on the program MINUIT [51] is described in detail elsewhere [50].

Results and Discussion
The assessment of thermal transformation of pure YFC xerogel and its co-mixture with LSM was analyzed by the XRD powder diffraction method. Calcination of the assynthesized, bottle-green xerogel at 950 • C resulted in the formation of a highly crystalline YFe 0.5 Co 0.5 O 3 perovskite structure with orthorhombic Pnma symmetry [52], whereas xerogel sintered at 1100 • C additionally contained a small amount of Y 2 O 3 (Figure 2) pointing at the partial decomposition of YFC. A thorough analysis of the XRD pattern ( Figure 2) indicated a slight difference in phase composition of LSM/YFC mixture as a function of calcination temperature. The diffraction pattern of the LSM and YFC mixture sintered at 950 • C for 2 h showed reflections belonging to La 0.775 Sr 0.225 MnO 3.047 [53] and YFe 0.5 Co 0.5 O 3 [52] phases. Sintering the LSM/YFC mixture at 1100 • C for two hours resulted in the appearance of new oxide phases due to chemical reactions in the solid state.
with AC voltage signal of 5 or 20 mV rms. Data treatment based on the program MINUIT [51] is described in detail elsewhere [50].

Results and Discussion
The assessment of thermal transformation of pure YFC xerogel and its co-mixture with LSM was analyzed by the XRD powder diffraction method. Calcination of the assynthesized, bottle-green xerogel at 950 °C resulted in the formation of a highly crystalline YFe0.5Co0.5O3 perovskite structure with orthorhombic Pnma symmetry [52], whereas xerogel sintered at 1100 °C additionally contained a small amount of Y2O3 (Figure 2) pointing at the partial decomposition of YFC. A thorough analysis of the XRD pattern ( Figure 2) indicated a slight difference in phase composition of LSM/YFC mixture as a function of calcination temperature. The diffraction pattern of the LSM and YFC mixture sintered at 950 °C for 2 h showed reflections belonging to La0.775Sr0.225MnO3.047 [53] and YFe0.5Co0.5O3 [52] phases. Sintering the LSM/YFC mixture at 1100 °C for two hours resulted in the appearance of new oxide phases due to chemical reactions in the solid state.
Analysis of the XRD pattern ( Figure 2) indicated that the LSM/YFC mixture sintered at 1100 °C is composed of a mixture of crystalline Sr4Fe4O11, YMnO3, and La0.775Sr0.225MnO3.047 oxide phases. The presence of the Sr4Fe4O11 phase is uncertain due to its reflections appearing at the same 2θ values as reflections of the LSM phase. However, the increase in the intensity of reflection at 32.70° of 2θ may confirm its contribution.  The morphology of obtained YFC perovskite powders is presented in Figure 3. The highly crystallized perovskite structure obtained after calcination at 950 • C consists of small, several millimeter-long fragile wafer-like pieces and revealed a specific surface area of 6 m 2 g −1 . The increase in sintering temperature up to 1100 • C caused a merging of small structures into larger ones accompanied by a decrease in BET surface area to 4 m 2 g −1 .   boundary resistance is visible (Figure 5d-f). The electrode part of impedance spectra consists of one (Figure 5b,c) or two (Figure 5a,d-f) overlapped capacitive semicircles. According to Wang et al. [54], the LSM electrode spectra can be divided into up to three semicircles representing electrode processes. The HF semicircle represents the charge transfer process, the medium frequency (MF) semicircle, the oxygen ion transfer on the electrodeelectrolyte interface, and the low frequency (LF) semicircle surface-exchange reaction on the cathode's surface consisting of dissociative adsorption of oxygen, ionization of adsorbed oxygen atoms to O 2-ions, and incorporation of these ions into the LSM electrode. The other authors [17] ascribed the LF process to gas diffusion according to the Adler-Lane-Steele Model [43].  Examples of recorded EIS spectra are presented in Figure 5. In the majority of EIS spectra recorded at higher temperatures (above 725 • C), the inductive loop caused by cable inductance appears (Figure 5b,c), whereas in spectra recorded at lower temperatures, a part of high-frequency (HF) capacitive semicircle connected to the electrolyte grain boundary resistance is visible (Figure 5d-f). The electrode part of impedance spectra consists of one (Figure 5b,c) or two (Figure 5a,d-f) overlapped capacitive semicircles. According to Wang et al. [54], the LSM electrode spectra can be divided into up to three semicircles representing electrode processes. The HF semicircle represents the charge transfer process, the medium frequency (MF) semicircle, the oxygen ion transfer on the electrode-electrolyte interface, and the low frequency (LF) semicircle surface-exchange reaction on the cathode's surface consisting of dissociative adsorption of oxygen, ionization of adsorbed oxygen atoms to O 2− ions, and incorporation of these ions into the LSM electrode. The other authors [17] ascribed the LF process to gas diffusion according to the Adler-Lane-Steele Model [43]. The obtained spectra were analyzed by the complex nonlinear least-squares method. Used electrical equivalent circuits (EECs) presented in Figure 5g,h are divided into two parts connected in series. The first electrolyte part contains resistor R0, which represents the resistance of lead cables and the part of the electrolyte resistance that is not visible in the frequency range of the recorded spectrum, whole or the grain interior electrolyte resistance, and coil L (Figure 5e) concerning the spectra in which the inductive loop representing the inductance of the cables is present. Each capacitive semicircle in the spectra is represented in EEC by a subcircuit consisting of a parallel-connected resistor (R) and a constant phase element (CPE).
The semicircle connected with the impedance of the grain boundary of the SDC electrolyte resistance observed in a part of the spectra is represented by the (RGB and CPEGB) subcircuit. The electrode part of the EEC consists of two (R1 and CPE1) and (R2 and CPE2) or one (R1 and CPE1) subcircuit for spectra with two (Figure 5a,d-f) or one (Figure 5b,c) Figure 5. Example of recorded EIS spectra: (a-c) t 800 • C and P(O 2 ) P −1 = 1, 0.2, 0.05, and 0.01 for black, green, red, and blue, respectively; (d-f) at P(O 2 ) P −1 = 0.2, and at 650, 625, and 600 • C-for black, green, and red, respectively; (a,d) LSM2 cathode; (b,e) LSM1 cathode; (c,f) LSM cathode; crosses experimental points, circles fitted points, numbers above enlarged crosses denote the logarithm of the frequency, and (g,h) electrical equivalent circuits used for fitting spectra; all spectra are shifted along the x-axis near the origin to facilitate comparisons.
The obtained spectra were analyzed by the complex nonlinear least-squares method. Used electrical equivalent circuits (EECs) presented in Figure 5g,h are divided into two parts connected in series. The first electrolyte part contains resistor R 0 , which represents the resistance of lead cables and the part of the electrolyte resistance that is not visible in the frequency range of the recorded spectrum, whole or the grain interior electrolyte resistance, and coil L (Figure 5e) concerning the spectra in which the inductive loop representing the inductance of the cables is present. Each capacitive semicircle in the spectra is represented in EEC by a subcircuit consisting of a parallel-connected resistor (R) and a constant phase element (CPE).
The semicircle connected with the impedance of the grain boundary of the SDC electrolyte resistance observed in a part of the spectra is represented by the (R GB and CPE GB ) subcircuit. The electrode part of the EEC consists of two (R 1 and CPE 1 ) and (R 2 and CPE 2 ) or one (R 1 and CPE 1 ) subcircuit for spectra with two (Figure 5a,d-f) or one (Figure 5b,c) semicircle in the electrode parts, respectively. The polarization resistance R p was calculated as the sum of resistances representing electrode processes R p = R 1 + R 2 for two or R p = R 1 for one (R and CPE) subcircuit in the electrode part of the EEC.
LSM does not react with YFC at 950 • C; however, it sinters very poorly at this temperature. The cathodes obtained at 950 • C were characterized by a very high R p ; thus, the results presented below concern only the cathodes obtained at 1100 • C.
The dependency of polarization resistance on temperature is presented in the Arrhenius plot (Figure 6). LSM1 and LSM2 cathodes attain polarization resistances lower and greater than the LSM one, respectively, in the entire examined temperature range. Moreover, the differences between the polarization resistances of LSM, LSM1 and LSM2 electrodes increase with decreasing temperature due to differences in the values of its activation energy (E a ). Activation energies of reciprocal polarization resistances in the range of 500-800 • C are equal to 1.34, 1.33, and 1.58 eV for LSM, LSM1, and LSM2 cathodes, respectively. Huber et al. [55] reported an E a of 1.4 eV for LSM in the range below 700 • C. semicircle in the electrode parts, respectively. The polarization resistance Rp was calculated as the sum of resistances representing electrode processes Rp = R1 + R2 for two or Rp = R1 for one (R and CPE) subcircuit in the electrode part of the EEC. LSM does not react with YFC at 950 °C; however, it sinters very poorly at this temperature. The cathodes obtained at 950 °C were characterized by a very high Rp; thus, the results presented below concern only the cathodes obtained at 1100 °C.
The dependency of polarization resistance on temperature is presented in the Arrhenius plot (Figure 6). LSM1 and LSM2 cathodes attain polarization resistances lower and greater than the LSM one, respectively, in the entire examined temperature range. Moreover, the differences between the polarization resistances of LSM, LSM1 and LSM2 electrodes increase with decreasing temperature due to differences in the values of its activation energy (Ea). Activation energies of reciprocal polarization resistances in the range of 500-800 °C are equal to 1.34, 1.33, and 1.58 eV for LSM, LSM1, and LSM2 cathodes, respectively. Huber et al. [55] reported an Ea of 1.4 eV for LSM in the range below 700 °C. In order to identify the influence of YFC addition on different rate-limiting steps of the ORR, resistance dependency associated with each response was studied as a function of P(O2). The dependence of the resistance associated with the i-th process on oxygen concentration is described by the following formula: where a and m are coefficients. The m value is the reaction order and provides information about oxygen species involved in this stage of the electrode reaction [17,[56][57][58][59][60]. In order to identify the influence of YFC addition on different rate-limiting steps of the ORR, resistance dependency associated with each response was studied as a function of P(O 2 ). The dependence of the resistance associated with the i-th process on oxygen concentration is described by the following formula: where a and m are coefficients. The m value is the reaction order and provides information about oxygen species involved in this stage of the electrode reaction [17,[56][57][58][59][60]. The dependencies of the fitted parameters on the oxygen pressure at 800 • C are shown in Figure 7. The EECs containing either three or two (R, CPE) subcircuits were tested for fitting EIS spectra of the LSM electrode. Results were characterized by standard deviation in the range from 0.11 to 0.98% and 0.62-2.03%, respectively. Therefore, the EEC containing three (R, CPE) subcircuits was chosen for the LSM cathode. Figure 7b-d show the values of the fitted parameters. C GB , R GB , and α GB are constant across the entire concentration range, and their values are typical for GB SDC electrolyte impedance [49] for all spectra where GB semicircle appeared. R 1 and R 2 are oxygen concentration dependent and characterized by reaction orders close to 0.375, which is characteristic for the one-electron charge-transfer process (Figure 7b). Both processes are characterized by an identical dependence on oxygen pressure within the measurement error and small differences in capacity, however, coefficients α are very different, e.g., around 0.5 and 0.9, causing the difference in semicircle shapes. Therefore, it should not be treated as a single process. Yan et al. [61] observed that surface exchange reaction depends on the crystallographic surface on which it occurs. These authors proposed two parallel surface exchange mechanisms.

Conclusions
In this study, highly porous composite cathodes made of LSM and YFC for IT SOFCs were obtained for the first time. The following conclusions are made: 1. The sintering of YFC xerogel at 950 °C results in the formation of a pure, highly crystalline, wafer-like perovskite structure. Composite cathodes sintered at 950 °C LSM1 The EEC containing two (R, CPE) subcircuits was used for fitting EIS spectra of the LSM1 electrode. The results were characterized by a standard deviation in the range from 0.18 to 0.42. R 1 is oxygen-concentration dependent and characterized by reaction order m = 0.41, which is higher than for the pure LSM cathode. The slightly distorted capacitive semicircle assigned to the electrode reaction consists of two overlapped semicircles representing processes of different reaction orders 0.375 and 0.5. The increase in the order of the reaction caused by small YFC additions means that the resistance caused by dissociation of adsorbed oxygen molecules has a greater share. Since the entire resistance decreased simultaneously, we conclude that it is caused by a decrease in resistance associated with the one-electron charge-transfer process.
The EEC containing two (R, CPE) subcircuits in its electrode part is used for fitting EIS spectra of the LSM2 electrode. The results were characterized by a standard deviation in the range from 0.29 to 0.66%. R 1 is oxygen-concentration dependent and characterized by reaction order m = 0.33 (m = 0.39 in the range P(O 2 ) P −1 from 0.1 to 1); R 2 is almost oxygen-concentration independent with m = 0.06, which confirms that the MF process constitutes oxygen ion transfer on the electrode-electrolyte interface (m = 0 [60]).
The EEC containing two (R, CPE) subcircuits was used for fitting EIS spectra for LSM and LSM1 electrodes at 700 • C as well as three (R, CPE) subcircuits for LSM2. The orders of reactions at this temperature are similar to those obtained at 800 • C. For LSM and LSM1 cathodes, m = 0.41 and m = 0.43 were obtained, respectively, whereas for LSM2, R 1 is characterized by reaction order m = 0.36 (m = 0.43 in the range P(O 2 ) P −1 from 0.1 to 1) and m = 0.08 for R 2 .

Conclusions
In this study, highly porous composite cathodes made of LSM and YFC for IT SOFCs were obtained for the first time. The following conclusions are made: 1.
The sintering of YFC xerogel at 950 • C results in the formation of a pure, highly crystalline, wafer-like perovskite structure. Composite cathodes sintered at 950 • C LSM1 (5 wt% YFC-95 wt% LSM) and LSM2 (50 wt% YFC-50 wt% LSM) maintained both components' structure; however, they were characterized by very high polarization resistance.

2.
The increase in sintering temperature up to 1100 • C causes the disintegration of perovskite crystals and the creation of Sr 4 Fe 4 O 11 and YMnO 3 mixed oxide phases. These cathodes reveal acceptably low polarization resistance and activation energies equal to 1.34, 1.33, and 1.58 eV for LSM, LSM1, and LSM2 respectively. 3.
The 5 wt% addition of YFC to LSM cathodes results in a decrease in polarization resistance. The decrease is probably caused by the facilitation of the charge transfer process. The decrease becomes larger with a decrease in temperature and with an increase in oxygen concentration.  Institutional Review Board Statement: Not applicable.
Informed Consent Statement: Not applicable.

Data Availability Statement:
The data presented in this study are available upon request from the corresponding authors.

Conflicts of Interest:
The authors declare no conflict of interest.