GDC-Based Inﬁltrated Electrodes for Solid Oxide Electrolyzer Cells (SOECs)

: In this work, porous complex and metal-free cathodes based on a (La 0.6 Sr 0.4 ) (Cr 0.5 Mn 0.5 ) O 3 (LSCM) screen-printed backbone inﬁltrated with Ce 0.9 Gd 0.1 O 2 (GDC) were fabricated for solid oxide electrolyzer cells. GDC inﬁltration has been optimized by structural and microstructural investigation and tested by electrochemical measurements in CO / CO 2 mixtures. Inﬁltrated electrodes with a non-aqueous GDC solution showed the best electro-catalytic activity towards CO 2 reduction, exhibiting a much lower polarization resistance, i.e., R pol = 0.3 Ω · cm 2 at 900 ◦ C. The electrochemical performance of LSCM / GDCE in terms of R pol is comparable to the best-performing Ni-YSZ cathode in the same operating conditions (R pol = 0.23 Ω · cm 2 ).


Introduction
The electrochemical conversion of CO 2 for fuels and chemical production is one of the most promising methods for greenhouse gas recycling and reutilization [1]. Unfortunately, it is known that low-temperature electrochemical processes exhibit several major issues related to slow reaction kinetic, the strict control of operating conditions, and catalyst poisoning [2][3][4]. Low-temperature electrochemical processes for CO 2 reduction involving molecular catalysts or non-aqueous solvent systems have also been proposed, but they show some major drawbacks such as high costs and low current densities [5][6][7]. Otherwise, high-temperature solid oxide electrolyzer cells (SOECs) show several positive features: firstly, SOECs are whole-ceramic devices and do not make use of liquid electrolytes, avoiding the problem of leakage and corrosion [8,9]. Then, the high operating temperature favors the kinetic at the electrodes and increases the overall efficiency of the cells [10]. Finally, SOECs can exploit all advantages of the development of solid oxide fuel cell (SOFC) materials [11][12][13] and technologies [14,15]. Therefore, extensive studies of SOECs and CO 2 electrolysis are largely available in the recent literature [1,16,17], as durable, stable, and efficient working electrodes for SOEC are greatly required.
Nickel/yttria stabilized zirconia (Ni-YSZ) has been widely investigated and proposed as the best cathode material for SOECs, mainly because of its very good ionic and electronic conductivity, high catalytic activity, low cost, and an expansion coefficient comparable to those of other cell components. Despite the high CO 2 conversion efficiency, however, Ni-based electrodes have shown some severe limitations due to the strict requirements of fuel compositions 2 of 11 (to avoid Ni oxidation) and the carbon coke formation [18]. To replace Ni-based electrodes, perovskite materials such as variously doped lanthanum chromites or lanthanum ferrites and their mixtures have been recently investigated. They show good stability in carbon-rich environments and promising electro-catalytic activity for CO 2 conversion [19,20]. For example, perovskite oxides such as (La 0.75 Sr 0.25 ) 0.95 Cr 0.5 Mn 0.5 O 3-δ [21], La 0.35 Sr 0.65 TiO 3-δ [22], La 0.6 Sr 0.4 VO 3-δ [23], and Sr 2 Fe 1.5 Mo 0.5 O 6-δ [24] can represent valid alternatives to Ni-YSZ cathodes. In particular, these perovskite oxides exhibit high mixed electronic and ionic conductivity, very good redox stability, and a very high resistance to both sulfur poisoning and coke formation. Unfortunately, such perovskite-based cathodes do not reach a CO 2 electrolysis performance comparable to Ni-YSZ cathodes, mainly because of their reduced electrocatalytic activity.
However, recently, a novel composite cathode based on lanthanum strontium chromium manganite (LSCM)/gadolinium-doped ceria (GDC) seems to be a good alternative to Ni-YSZ cathodes [25]. It was already reported that the infiltration of GDC nanoparticles into the LSCM backbone is crucial because it increases the triple-phase boundaries (TPBs) and favors the CO 2 chemical adsorption [26,27], enhancing the electrochemical CO 2 dissociation. Nevertheless, the agglomeration of doped-ceria nanoparticles occurring upon preparation and/or long-term runs can affect the stability of the cell. Moreover, the morphological properties of GDC-infiltrated powders may also depend on the starting solutions used for the infiltration into the LSCM backbone [28]. Generally speaking, oxide particles precipitated from aqueous solutions often show a tendency to agglomerate [29,30] and, in the case of ceria-based systems, the use of non-aqueous solutions can give some advantages in terms of the morphology of the infiltrated powders [31].
In this work, we investigated the influence of different infiltrating solutions upon the electrode microstructure. Thus, aqueous and ethanol GDC solutions were used for the infiltration of the LSCM backbone deposited on an 8 mol% Y 2 O 3 -doped ZrO 2 (8YSZ) electrolyte. The morphology of the electrodes and the electrochemical performance of the cells are investigated and discussed.

Materials and Methods
8 mol% Y 2 O 3 -doped ZrO 2 (8YSZ) powders purchased from Tosoh were used as an electrolyte. The powders were uniaxially pressed into pellets and sintered at 1500 • C for 3 h using a heating rate of 2 • C/min. The density of the sintered pellets, measured with a hydrostatic balance, was 5.86 g/cm 3 (about 97% of the theoretical value). Thick electrodes were screen-printed onto both sides of the pellets. Scandium-doped Zirconia (ScSZ, Pi-Kem Ltd.-Tamworth, UK), YSZ (Tosoh-Tokyo, Japan), and Lanthanum Strontium Manganite (LSM, Pi-Kem Ltd.-Tamworth, UK) were employed for anode preparation and Lanthanum Strontium Chromium Manganite (LSCM, Pi-Kem Ltd.-Tamworth, UK) for the cathode. Inks for deposition were prepared by ball milling each powder with a dispersant (Polyester/Polyamide Copolymer Dispersant, KD-1) and organic binders (Terpineol and Decoflux WB41) [32]. Glassy carbon and graphite were used as a pore former. A total of 30 wt% of pore former was necessary to get sufficient porosity for infiltration. Solutions (2 M) of 10% mol Gd-doped CeO 2 (GDC10) were prepared for the cathode impregnation. Proper amounts of Ce(NO 3 ) 3 ·6H 2 O (Sigma-Aldrich-Steinheim, Germany) and Gd(NO 3 ) 3 ·6H 2 O (Sigma Aldrich-Steinheim, Germany), i.e., 19,537 and 2256 g for cerium nitrate and gadolinium nitrate, respectively, were dissolved into 25 mL of either distilled water (GDCW solution) or into pure ethanol (GDCE solution). Thus, the two solutions used for infiltration are named: GDCW and GDCE.
For the cathode fabrication, a thin first layer of YSZ was screen-printed onto the YSZ electrolyte pellet to favor a good adhesion with the overlaying LSCM layer. The deposited layers were soaked at 800 • C for 1 h to remove any undesired carbon residues and then co-fired at 1300 • C for 2 h. For the anode fabrication, a ScSZ layer was firstly screen-printed and then an LSM layer was successively added. Each layer was soaked at 800 • C for 1 h and the bilayer was co-fired at 1100 • C for 2 h using a heating rate of 2 • C/min. The thickness of both bilayer electrodes was about 30-40 µm.
The LSCM/YSZ backbone was infiltrated using two GDC precursor solutions. The infiltration steps were carried out at room temperature and at atmospheric pressure. After each infiltration step, a thermal treatment at 500 • C for 45 min was performed to let the nitrates decompose. After each firing, the cell was weighted in order to get the final GDC loading equal to 50% of the YSZ/LSCM bilayer weight. A final calcination step of 1 h at 1100 • C was performed.
Structural and microstructural characterizations of infiltrated cathodes were performed. X-Ray Diffraction (XRD) analysis was carried out with a X-Pert Pro 500 diffractometer (Philips-Amsterdam, Nederlands) to evaluate the presence of the undesirable crystalline phases. Field emission-scanning electron microscopy (FE-SEM) using a Leo Supra 35 (Zeiss-Oberkochen, Germany) was used to investigate the grain size and distribution of the GDC particles infiltrated into the LSCM/YSZ cathode.
For electrochemical measurements, the cells were fastened onto an alumina tube using a gas-tight ceramic paste (curing treatment of 150 • C for 3 h). Au paste and wires were used as current collectors. Electrochemical impedance spectroscopy (EIS) measurements at open circuit voltage (OCV) were collected using a frequency response analyzer (FRA, Solartron 1260-Solartron Analytical-Leicester, UK) coupled with a dielectric interface (Solartron 1296-Solartron Analytical-Leicester, UK) with a frequency range of between 0.1 Hz and 1 MHz and an AC voltage amplitude of 100 mV. The measurements were carried out in the 700-800 • C temperature range, exposing the cathode to a 30/70 volume ratio of CO/CO 2 and the anode to static air.

Results and Discussion
GDC loading by infiltration varies considerably when using water and ethanol as solvents. Figure 1 shows the GDC loading percentage vs. the number of infiltrations by using the GDCW and GDCE solutions. The infiltrated cathodes are named LSCM/GDCW and LSCM/GDCE. The target value corresponding to the 50 wt% of the YSZ/LSCM weight is 100%. By using the GDCE solution, the desired amount of GDC loading was reached with five infiltrations, while eight infiltrations were necessary for the GDCW solution. For each infiltration step, the same liquid volume was selected. Moreover, the difference in the wetting behavior of the electrode support at each infiltration step is noteworthy. In fact, the GDCE droplets almost immediately diffused all over the support surface, while the liquid-solid interaction between the support and GDCW was significantly lower, as the liquid droplets had to be gently deposited in different electrode sites to obtain a homogeneous distribution of the infiltrated volume. The GDCE infiltration process produced a constant rate loading, while the GDCW infiltration showed a strongly non-linear loading evolution. The linear trend in the case of the GDCE suggests that the superficial region of the sample is substantially unaltered by the sequence of the infiltration steps, whereas the parabolic behavior likely indicates the formation of some barriers that reduce the further loading. Stoyanova et al. observed that factors such as the volatility of the impregnating medium (solution) may affect the distribution of the impregnated phase, i.e., ethanol ensured a small blocking effect of the porous texture and, thus, a high specific surface area of the impregnated phase [33].
The LSCM/GDCW-and LSCM/GDCE-infiltrated cathodes with the same GDC amount were investigated by XRD analysis. Figure 2 shows the XRD pattern of the LSCM/GDCW infiltrated cell. The LSCM/GDCE cell exhibits an identical diffraction pattern and thus, for reasons of clarity, it is not reported. All peaks belong to the 8YSZ (ICDD card n. 30-1468), GDC (ICDD card n. 75-161), and LSCM (ICDD card n. 86-1552) phases and no secondary phase has been revealed. Cerium and gadolinium mixed in the proper amount into the infiltrating solution formed a perfect homogeneous solid solution with a mild calcination step. The crystallographic parameter of cubic GDC was determined using UnitCell software [34]. The calculated value was 0.54177(1) nm in very good agreement with the theoretical value (0.5418 nm according to ICDD card n. 75-161), confirming the homogeneous dissolution of Gd 3+ cations in the fluorite lattice of ceria. The crystallite size was calculated using the Scherrer equation for the most intense peak, i.e., (111) at 2θ = 28.5 • . The size was about 80 nm for Appl. Sci. 2020, 10, 3882 4 of 11 both the LSCM/GDCW and LSCM/GDCE cathodes, meaning that no significant difference in the grain size was detectable for the two impregnation methods. The LSCM/GDCW-and LSCM/GDCE-infiltrated cathodes with the same GDC amount were investigated by XRD analysis. Figure 2 shows the XRD pattern of the LSCM/GDCW infiltrated cell. The LSCM/GDCE cell exhibits an identical diffraction pattern and thus, for reasons of clarity, it is not reported. All peaks belong to the 8YSZ (ICDD card n. 30-1468), GDC (ICDD card n. 75-161), and LSCM (ICDD card n. 86-1552) phases and no secondary phase has been revealed. Cerium and gadolinium mixed in the proper amount into the infiltrating solution formed a perfect homogeneous solid solution with a mild calcination step. The crystallographic parameter of cubic GDC was determined using UnitCell software [34]. The calculated value was 0.54177(1) nm in very good agreement with the theoretical value (0.5418 nm according to ICDD card n. 75-161), confirming the homogeneous dissolution of Gd 3+ cations in the fluorite lattice of ceria. The crystallite size was calculated using the Scherrer equation for the most intense peak, i.e., (111) at 2θ = 28.5°. The size was about 80 nm for both the LSCM/GDCW and LSCM/GDCE cathodes, meaning that no significant difference in the grain size was detectable for the two impregnation methods.   Microstructural analyses of the cathode/electrolyte interface and cathode surface were performed. Figure 3 shows the SEM micrograph of a 30 μm thick LSCM/GDCW cross section. A very good adhesion between cathode and electrolyte is reasonably revealed due to the presence of a thin YSZ screen-printed layer. The same features (not reported) were also revealed for the LSCM/GDCE cathode, indicating that no significant difference appears from the cross-section analysis. Microstructural analyses of the cathode/electrolyte interface and cathode surface were performed. Figure 3 shows the SEM micrograph of a 30 µm thick LSCM/GDCW cross section. A very good adhesion between cathode and electrolyte is reasonably revealed due to the presence of a thin YSZ screen-printed layer. The same features (not reported) were also revealed for the LSCM/GDCE cathode, indicating that no significant difference appears from the cross-section analysis. Microstructural analyses of the cathode/electrolyte interface and cathode surface were performed. Figure 3 shows the SEM micrograph of a 30 μm thick LSCM/GDCW cross section. A very good adhesion between cathode and electrolyte is reasonably revealed due to the presence of a thin YSZ screen-printed layer. The same features (not reported) were also revealed for the LSCM/GDCE cathode, indicating that no significant difference appears from the cross-section analysis.    At low magnification, the LSCM/GDCE surface ( Figure 4A) seems porous, with the presence of micrometric clusters ( Figure 4B) covered by GDC nanometric grains of about 100 nm ( Figure 4C). The measured size value is very similar to the GDC crystallite size calculated using the Scherrer equation.
Otherwise, the LSCM/GDCW surface shows dense and compact zones separated by micrometric cracks (Figure 5A). At higher magnification, the LSCM/GDCW compact areas look quite dense ( Figure 5B), different to the LSCM/GDCE ( Figure 4B). Thus, agglomeration phenomena tend to fill up the surface porosity and these features reasonably occur after each calcination step. The tendency to agglomerate is well known for oxides deriving from aqueous solution precipitation [29][30][31]. To overcome this limitation, the use of some final washing cycles with ethanol can remove the water molecules from the surface of the particles and hinder the formation of an oxo-bridging bond [35].
Thus, when an aqueous solution was used for the infiltration, the GDC did not properly penetrate inside the porous LSCM backbone and only a small amount of the GDC reached the At low magnification, the LSCM/GDCE surface ( Figure 4A) seems porous, with the presence of micrometric clusters ( Figure 4B) covered by GDC nanometric grains of about 100 nm ( Figure 4C). The measured size value is very similar to the GDC crystallite size calculated using the Scherrer equation.
Otherwise, the LSCM/GDCW surface shows dense and compact zones separated by micrometric cracks (Figure 5A). At higher magnification, the LSCM/GDCW compact areas look quite dense ( Figure 5B), different to the LSCM/GDCE ( Figure 4B). Thus, agglomeration phenomena tend to fill up the surface porosity and these features reasonably occur after each calcination step. The tendency to agglomerate is well known for oxides deriving from aqueous solution precipitation [29][30][31]. To overcome this limitation, the use of some final washing cycles with ethanol can remove the water molecules from the surface of the particles and hinder the formation of an oxo-bridging bond [35].
Thus, when an aqueous solution was used for the infiltration, the GDC did not properly penetrate inside the porous LSCM backbone and only a small amount of the GDC reached the interface with the electrolyte. Figure 5C,D confirms the presence of dispersed and not interconnected GDC nanoparticles in the interior electrode.
Thus, the microstructure observed can be related to the infiltration procedure reported in Figure 1. The constant GDC loading and the reduced number of infiltrations of the GDCE are in agreement with the observed open-surface porosity that induces a continuous GDC pathway in the backbone; differently, the non-linear loading and the larger amount of infiltration of the GDCW can be related to a less porous electrode surface that prevents a proper and homogeneous infiltration. So, in the LSCM/GDCW cathode, the GDC particles stack together on the external surface of the electrode, while in the LSCM/GDCE a much more uniform distribution of Gd-doped ceria inside the electrode occurs.
Therefore, the noticeable morphological differences emerging from the SEM micrographs between infiltrated cathodes may affect the electrochemical behavior. Figure 6 shows the Nyquist plots at OCV of the LSCM/GDCW and LSCM/GDCE cells operating in a CO/CO 2 = 30/70 mixture in the 700-800 • C temperature range. As commonly reported, the impedance spectra show depressed semicircles due to the overlapping of different electrochemical phenomena. Table 1 reports the electrochemical data of the LSCM/GDCW and LSCM/GDCE cells: the ohmic resistance (R ohm ) being the high frequency intercept with the real axis, and the polarization resistance (R pol ) corresponding to the difference between the high and low frequency intercepts. interface with the electrolyte. Figure 5C,D confirms the presence of dispersed and not interconnected GDC nanoparticles in the interior electrode. Thus, the microstructure observed can be related to the infiltration procedure reported in Figure  1. The constant GDC loading and the reduced number of infiltrations of the GDCE are in agreement with the observed open-surface porosity that induces a continuous GDC pathway in the backbone; differently, the non-linear loading and the larger amount of infiltration of the GDCW can be related to a less porous electrode surface that prevents a proper and homogeneous infiltration. So, in the LSCM/GDCW cathode, the GDC particles stack together on the external surface of the electrode, while in the LSCM/GDCE a much more uniform distribution of Gd-doped ceria inside the electrode occurs.
Therefore, the noticeable morphological differences emerging from the SEM micrographs between infiltrated cathodes may affect the electrochemical behavior. Figure 6 shows the Nyquist plots at OCV of the LSCM/GDCW and LSCM/GDCE cells operating in a CO/CO2=30/70 mixture in the 700-800 °C temperature range. As commonly reported, the impedance spectra show depressed semicircles due to the overlapping of different electrochemical phenomena. Table 1 reports the electrochemical data of the LSCM/GDCW and LSCM/GDCE cells: the ohmic resistance (Rohm) being the high frequency intercept with the real axis, and the polarization resistance (Rpol) corresponding to the difference between the high and low frequency intercepts. At all temperatures investigated, the Rohm and Rpol values of the LSCM/GDCE are lower than those of the LSCM/GDCW. The ohmic resistance (Rohm) is mainly ascribable to the electrolyte but it can be also due to the ohmic contribution of electrodes, thus it is likely that the larger Rohm values of the LSCM/GDCW cell can be ascribable to the agglomeration of GDC nanoparticles on the cathode surface that enhance the ohmic resistance.   At all temperatures investigated, the R ohm and R pol values of the LSCM/GDCE are lower than those of the LSCM/GDCW. The ohmic resistance (R ohm ) is mainly ascribable to the electrolyte but it can be also due to the ohmic contribution of electrodes, thus it is likely that the larger R ohm values of the LSCM/GDCW cell can be ascribable to the agglomeration of GDC nanoparticles on the cathode surface that enhance the ohmic resistance.
At very low frequencies, the impedance spectra of the two cells are quite different. All EIS measurements show at least two semicircles from which it is possible to get the intercept with the real axis at a low frequency and thus evaluate the R pol values. The LSCM/GDCE cell exhibits impedance spectra comparable to the best performing literature data for similar cells [19,27], while the LSCM/GDCW shows an incomplete Warburg-like behavior at low frequencies, indicating unrestricted diffusion phenomena. Thus, the CO 2 reduction process mostly occurs at the LSCM/GDCE porous cathode and it is related to the cathode microstructure made of well dispersed and interconnected GDC nanoparticles that increase the TPB sites for CO 2 reduction [19].
In order to compare the LSCM/GDCE performance with the state-of-art, the cell has been specifically tested at 900 • C. Figure 7 shows the Nyquist plot of the LSCM/GDCE cell operating with a CO/CO 2 = 30/70 mixture at 900 • C alongside the related fitted plot, obtained via software simulation by using the equivalent circuit reported in the inset.
Appl. Sci. 2019, 9, x FOR PEER REVIEW 9 of 12 At very low frequencies, the impedance spectra of the two cells are quite different. All EIS measurements show at least two semicircles from which it is possible to get the intercept with the real axis at a low frequency and thus evaluate the Rpol values. The LSCM/GDCE cell exhibits impedance spectra comparable to the best performing literature data for similar cells [19,27], while the LSCM/GDCW shows an incomplete Warburg-like behavior at low frequencies, indicating unrestricted diffusion phenomena. Thus, the CO2 reduction process mostly occurs at the LSCM/GDCE porous cathode and it is related to the cathode microstructure made of well dispersed and interconnected GDC nanoparticles that increase the TPB sites for CO2 reduction [19].
In order to compare the LSCM/GDCE performance with the state-of-art, the cell has been specifically tested at 900 °C. Figure 7 shows the Nyquist plot of the LSCM/GDCE cell operating with a CO/CO2 = 30/70 mixture at 900 °C alongside the related fitted plot, obtained via software simulation by using the equivalent circuit reported in the inset. The Nyquist plot was fitted with an LR1(CPE2R2)(CPE3R3) equivalent circuit, in which L is the inductance due to the wires of the instrument set up, R1 is the high-frequency intersection of the plot with the real axis and represents the ohmic resistance (Rohm) of the electrolyte and infiltrated cathode, R2 is the polarization resistance obtained from the high-frequency (HF) arc and is related to the charge transfer process at the electrode/electrolyte interface, and R3 is the polarization resistance from the low-frequency (LF) arc and is ascribable to non-charge transfer processes at the electrodes.
The overall polarization resistance (R2 + R3) value is 0.3 Ω‧cm 2 , which is comparable to the best performing cathodes from literature. In fact, the conventional Ni-YSZ cathode in the same experimental conditions shows a polarization resistance value of 0.23 Ω‧cm 2 and a modified GDCbased cathode with Pd co-catalyst exhibits Rpol = 0.24 Ω cm 2 [25]. The Nyquist plot was fitted with an LR 1 (CPE 2 R 2 )(CPE 3 R 3 ) equivalent circuit, in which L is the inductance due to the wires of the instrument set up, R 1 is the high-frequency intersection of the plot with the real axis and represents the ohmic resistance (R ohm ) of the electrolyte and infiltrated cathode, R 2 is the polarization resistance obtained from the high-frequency (HF) arc and is related to the charge transfer process at the electrode/electrolyte interface, and R 3 is the polarization resistance from the low-frequency (LF) arc and is ascribable to non-charge transfer processes at the electrodes.
The overall polarization resistance (R 2 + R 3 ) value is 0.3 Ω·cm 2 , which is comparable to the best performing cathodes from literature. In fact, the conventional Ni-YSZ cathode in the same experimental conditions shows a polarization resistance value of 0.23 Ω·cm 2 and a modified GDC-based cathode with Pd co-catalyst exhibits R pol = 0.24 Ω·cm 2 [25].
Finally, Figure 8 shows the Arrhenius plot related to the LSCM/GDCE polarization resistance, exhibiting a good linearity over the whole temperature range investigated (700-900 • C). From the linear fit, an activation energy of the polarization process equal to ∼160 kJ mol −1 can be derived. linear fit, an activation energy of the polarization process equal to ∼160 kJ mol can be derived.

Conclusions
Performing cathodes were fabricated by GDC infiltration into a two-layered LSCM/YSZ backbone. Different infiltrating solutions using water and ethanol as solvents (GDCW and GDCE) were employed, resulting in different microstructures. Specifically, the non-aqueous solution greatly favored the GDC nanoparticles' dispersion by reducing the grain agglomeration and increasing the TPB sites for the process of CO2 reduction. The GDCE also improved the GDC particles' interconnection, favoring the transfer process at the electrode/electrolyte interface. EIS measurements at OCV performed on both the LSCM/GDCW-and LSCM/GDCE-infiltrated cathodes showed that both the ohmic and polarization resistances of the LSCM/GDCE values were lower than those of the LSCM/GDCW at all temperatures investigated. Moreover, the polarization resistance value of the LSCM/GDCE cathode (0.3 Ω‧cm 2 at 900 °C) is comparable to the best performing cathodes. Thus, in agreement with the relevant literature, this work confirms that infiltrated cathodes are promising for

Conclusions
Performing cathodes were fabricated by GDC infiltration into a two-layered LSCM/YSZ backbone. Different infiltrating solutions using water and ethanol as solvents (GDCW and GDCE) were employed, resulting in different microstructures. Specifically, the non-aqueous solution greatly favored the GDC nanoparticles' dispersion by reducing the grain agglomeration and increasing the TPB sites for the process of CO 2 reduction. The GDCE also improved the GDC particles' interconnection, favoring the transfer process at the electrode/electrolyte interface. EIS measurements at OCV performed on both the LSCM/GDCW-and LSCM/GDCE-infiltrated cathodes showed that both the ohmic and polarization resistances of the LSCM/GDCE values were lower than those of the LSCM/GDCW at all temperatures investigated. Moreover, the polarization resistance value of the LSCM/GDCE cathode (0.3 Ω·cm 2 at 900 • C) is comparable to the best performing cathodes. Thus, in agreement with the relevant literature, this work confirms that infiltrated cathodes are promising for SOEC applications. Further improvements can be achieved by optimizing the infiltration parameters of the fabrication procedure.