Analysis of Soot Deposition Mechanisms on Nickel-Based Anodes of SOFCs in Single-Cell and Stack Environment

: Solid oxide fuel cells (SOFCs) can be fueled with various gases, including carbon-containing compounds. High operating temperatures, exceeding 600 ◦ C, and the presence of a porous, nickel-based SOFC anode, might lead to the formation of solid carbon particles from fuels such as carbon monoxide and other gases with hydrocarbon-based compounds. Carbon deposition on fuel electrode surfaces can cause irreversible damage to the cell, eventually destroying the electrode. Soot formation mechanisms are strictly related to electrochemical, kinetic, and thermodynamic conditions. In the current study, the e ﬀ ects of carbon deposition on the lifetime and performance of SOFCs were analyzed in-operando, both in single-cell and stack conditions. It was observed that anodic gas velocity has an impact on soot formation and deposition, thus it was also studied in depth. Single-anode-supported solid oxide fuel cells were fueled with gases delivered in such a way that the initial velocities in the anodic compartment ranged from 0.1 to 0.7 m / s. Both cell operation and post-mortem observations proved that the carbon deposition process accelerates at higher anodic gas velocity. Furthermore, single-cell results were veriﬁed in an SOFC stack operated in carbon-deposition regime by dry-coupling with a downdraft 150 kWth biomass gasiﬁer. Contributions: Conceptualization, K.M., M.S., M.W. and J.K.; Methodology, K.M., M.B. Blesznowski), M.S., M.W. and J.K.; Blesznowski),


Introduction
One of the key advantages of solid oxide fuel cells (SOFCs) is their fuel flexibility. The ability to convert hydrogen, carbonaceous, and hydrocarbon fuels privileges the application of these devices in energy transition technologies, where high efficiency and environmentally-friendly parameters must be secured. The elevated operating temperature in the range from 600 • C to 850 • C enhances the electrochemistry, catalyses chemical reactions, and guarantees usability of heat at the outlet of the SOFC unit [1]. This heat is used to preheat incoming streams of gases entering the fuel cells and can be used in the preparation of hot water or steam in cogenerative systems [2] or, optionally, can be used to drive an absorption chiller for the production of cold [3]. With these approaches SOFCs can be considered as prime movers in electricity generators, combined heat and power units (CHP), and combined heat, power and cooling systems (CCHP). Systems with SOFCs can be part of systems which enable carbon recovery and recycling for zero net carbon dioxide emissions by integration with algal systems for CO 2 utilization [4]. They can be employed in carbon capture and sequestration (CCS)-ready systems which integrate post-combustion processes of anodic lean gases with oxygen membranes to achieve high concentrations of carbon dioxide in exhaust gases [5]. These benefits make this technology attractive for stationary applications [6]. SOFC-based power units are characterized by electrical efficiency of 45% to 65%, whereas 37-45% is reported for conventional steam-cycles [7][8][9] and up to 60% for state-of-the-art natural gas combined cycles (NGCC). The electrical efficiency of systems with SOFCs can be elevated by fuel recirculation or by serial connection of fuel cell stacks [10]. Moreover, processes like waste incineration [11], anaerobic digestion [12], biomass gasification, and pyrolysis produce gases which can fuel SOFC plants [13][14][15]. For such fuels, minimal pre-processing like desulfurization [16,17] and pre-reforming [18] are required. Currently, such gases are mainly combusted in burners designed to accept the presence of hydrogen and impurities. SOFCs mitigate or avoid some of these problems, due to fuel conversion inside the cell. The anode's catalytic properties and the high operating temperature promote internal steam reforming of hydrocarbons like steam methane reforming (SMR) (Equation (1)) [19], dry reforming of carbon dioxide and methane (Equation (2)), [20] and the water gas shift reaction-WGS (Equation (3)) [21].
Apart from the many benefits of Ni-YSZ cermet, it also favors the formation of solid particles of carbon over its surface [22]. A nickel-based electrode is a very good catalyst for carbon formation reactions, such as the following: cracking of methane : CH 4 → C + 2H 2 (4) reduction of carbon monoxide : CO + H 2 ↔ C + H 2 O Boudouard reaction : 2CO → C + CO 2 (6) The increase of CO concentration in fuel enhances carbon deposition via the Boudouard reaction in the anode volume, as well as other stack elements and pipelines [23]. A similar effect is obtained when the SOFC is fueled with pure methane or methane-rich gases, due to the methane cracking reaction. Usually, tests with demanding fuels are performed by operating at high current densities in order to promote WGS reaction [24], higher fuel utilization [25], and at appropriate steam-to-carbon ratios (S/C) in order to keep carbon activity at near unity. Setting an appropriate S/C value helps to create operating conditions in which carbon deposition is thermodynamically unfavored. In typical SOFC power generation systems, the S/C ratio value is set to 2.2, as shown in Figure 1 [26][27][28]. One way to determine a safe value for this process is to use ternary diagrams with isotherms of carbon formation or Gibbs diagrams ( Figure 1). The thermodynamic boundary between non-deposition and deposition zones can be defined by determining the equilibrium composition for different gas mixtures, containing carbon, hydrogen, and oxygen atoms. Curves for different temperatures are presented in the diagram as isotherms of carbon formation [29]. Carbon deposition might occur in various conditions. Firstly, the formation of a solid carbon layer on the porous surface might affect the uniformity of flow distribution along the active area of the fuel cell [31]. Moreover, the thin layer of deposit leads to reduction of the active area or triple phase boundary (TPB) length involved in high temperature electrochemical processes [32]. In addition to affecting the outer surface, it can lead to an increase of exposure time to a significant deterioration of the physical and chemical properties of the material and functional layer of the anode [33].
Numerous groups applied the electrochemical impedance spectroscopy (EIS) technique for determining the cell parameters and degradation in methane-fueled anode-supported SOFCs. Chen et al. [34] demonstrated that operating conditions and composition of fuel influence the morphology of deposited carbon structures and the fuel cell degradation process. Their EIS measurements revealed that for the fuel cell with a Ni-YSZ anode fueled with syngas, the cell electrochemical performance degraded very rapidly after carbon was deposited. Koh J. et al. [35] presented that carbon deposition with humidified methane on a Ni-YSZ porous surface is reversible when it is oxidized at a current load in thermo-dynamically carbon-free conditions. They measured a shortterm (3 h) EIS evolution on a Ni-YSZ anode-supported cell fueled by a mixture of methane and nitrogen. The EIS measurement was realized under carbon-deposition-promoting conditions-at open circuit voltage (OCV) as well as at load, beyond the carbon deposition regime. The spectrum at OCV evolved strongly, especially in the beginning of the experiment. Operation at current revealed a stable spectra for 100 min. Lanzini et al. [32] investigated a Ni-YSZ-supported cell (diameter 80 mm) with a mixture of methane and CO2 for 250 h. Up to 200 h, the spectra change was linear and rather limited. After 200 h, carbon deposition caused a dramatic increase of the cell's area-specific resistance (ASR), leading the experiment to an end. Lyu et al. [36] investigated direct internal reforming (DIR) of methane and published EIS spectra of the anode-supported SOFCs (AS-SOFCs) tested at various S/C ratios. S/C above 0.5 revealed very good DIR-SOFC performance. Decreasing S/C to 0.5 and further (down to 0.03) resulted in a high ASR increase. From the reported data, lowering S/C slightly decreased cell ohmic resistance. Silva-Mosqueda et al. [37] investigated an AS-SOFC for 500 h, measuring impedance spectra. During the operation, an increase in the cell impedance was observed mainly in the intermediate frequencies.
Papurello et al. [38] investigated steam-reforming of simulated biogas (60% methane, 40% carbon dioxide) inside an SOFC anode. Numerous impedance spectra were presented including a mild H2S poisoning of the cell at 750 °C for 10 days (S/C = 1.0, 0.46 ppm H2S). The ohmic cell resistance decreased in time while the ASR increased significantly, which was addressed to sulfur poisoning and to a smaller extent, to carbon deposition. Carbon deposition might occur in various conditions. Firstly, the formation of a solid carbon layer on the porous surface might affect the uniformity of flow distribution along the active area of the fuel cell [31]. Moreover, the thin layer of deposit leads to reduction of the active area or triple phase boundary (TPB) length involved in high temperature electrochemical processes [32]. In addition to affecting the outer surface, it can lead to an increase of exposure time to a significant deterioration of the physical and chemical properties of the material and functional layer of the anode [33].
Numerous groups applied the electrochemical impedance spectroscopy (EIS) technique for determining the cell parameters and degradation in methane-fueled anode-supported SOFCs. Chen et al. [34] demonstrated that operating conditions and composition of fuel influence the morphology of deposited carbon structures and the fuel cell degradation process. Their EIS measurements revealed that for the fuel cell with a Ni-YSZ anode fueled with syngas, the cell electrochemical performance degraded very rapidly after carbon was deposited. Koh J. et al. [35] presented that carbon deposition with humidified methane on a Ni-YSZ porous surface is reversible when it is oxidized at a current load in thermo-dynamically carbon-free conditions. They measured a short-term (3 h) EIS evolution on a Ni-YSZ anode-supported cell fueled by a mixture of methane and nitrogen. The EIS measurement was realized under carbon-deposition-promoting conditions-at open circuit voltage (OCV) as well as at load, beyond the carbon deposition regime. The spectrum at OCV evolved strongly, especially in the beginning of the experiment. Operation at current revealed a stable spectra for 100 min. Lanzini et al. [32] investigated a Ni-YSZ-supported cell (diameter 80 mm) with a mixture of methane and CO 2 for 250 h. Up to 200 h, the spectra change was linear and rather limited. After 200 h, carbon deposition caused a dramatic increase of the cell's area-specific resistance (ASR), leading the experiment to an end. Lyu et al. [36] investigated direct internal reforming (DIR) of methane and published EIS spectra of the anode-supported SOFCs (AS-SOFCs) tested at various S/C ratios. S/C above 0.5 revealed very good DIR-SOFC performance. Decreasing S/C to 0.5 and further (down to 0.03) resulted in a high ASR increase. From the reported data, lowering S/C slightly decreased cell ohmic resistance. Silva-Mosqueda et al. [37] investigated an AS-SOFC for 500 h, measuring impedance spectra. During the operation, an increase in the cell impedance was observed mainly in the intermediate frequencies.
Papurello et al. [38] investigated steam-reforming of simulated biogas (60% methane, 40% carbon dioxide) inside an SOFC anode. Numerous impedance spectra were presented including a mild H 2 S poisoning of the cell at 750 • C for 10 days (S/C = 1.0, 0.46 ppm H 2 S). The ohmic cell resistance decreased in time while the ASR increased significantly, which was addressed to sulfur poisoning and to a smaller extent, to carbon deposition. Several publications mention different types of dopants that inhibit the carbon deposition process without influencing fuel cell performance [39][40][41][42][43].
The aim of this work is to compare the soot deposition mechanisms on the fuel electrode in a single-fuel-cell and stack environment in order to determine the correlation between operating parameters and cell degradation. Moreover, the results demonstrate the acceptable deviations from theoretically-safe fuel cell operating conditions.

Experimental Setup
To experimentally study carbon formation on the surface of nickel-based electrodes exposed to carbon-rich fuels, two approaches were proposed within the testing campaign. The first approach concerned single-cell experiments whereas the second one-the stack environment. In both cases, anode-supported SOFCs (AS-SOFCs) were used. However, the active area and thickness differed. In the case of a 1-mm-thick single cell, the active area was 16 cm 2 . A 5-cell stack was comprised of 0.55 mm thick cells with 92 cm 2 of active area per cell.
The experimental setups were operated in test stands consisting of an electric oven, gas analyzers (Siemens, Munich, Germany), electrochemical workstation (Zahner IM6ex+PP240, ZAHNER-elektrik, Kronach, Germany), electronic load (Chroma 63201, Chroma, Xiamen, China), and data acquisition system (temperatures, pressures, and voltages). The construction of the test stands differed in detail but provided similar functionality. In contrast to single-cell testing, the AS-SOFC stack was fueled in operando by syngas from a gasifier.

Single-Cell Testing
In the present work, custom-made planar AS-SOFCs (50 × 50 × 1 mm, 16 cm 2 active area) produced at the Institute of Power Engineering, Ceramic Department CEREL were used in the experimental analysis for single-cell testing [44,45]. A cross-section of the cell is shown in Figure 2 together with definitions of particular layers. Several publications mention different types of dopants that inhibit the carbon deposition process without influencing fuel cell performance [39][40][41][42][43]. The aim of this work is to compare the soot deposition mechanisms on the fuel electrode in a single-fuel-cell and stack environment in order to determine the correlation between operating parameters and cell degradation. Moreover, the results demonstrate the acceptable deviations from theoretically-safe fuel cell operating conditions.

Experimental Setup
To experimentally study carbon formation on the surface of nickel-based electrodes exposed to carbon-rich fuels, two approaches were proposed within the testing campaign. The first approach concerned single-cell experiments whereas the second one-the stack environment. In both cases, anode-supported SOFCs (AS-SOFCs) were used. However, the active area and thickness differed. In the case of a 1-mm-thick single cell, the active area was 16 cm 2 . A 5-cell stack was comprised of 0.55 mm thick cells with 92 cm 2 of active area per cell.
The experimental setups were operated in test stands consisting of an electric oven, gas analyzers (Siemens, Munich, Germany), electrochemical workstation (Zahner IM6ex+PP240, ZAHNER-elektrik, Kronach, Germany), electronic load (Chroma 63201, Chroma, Xiamen, China), and data acquisition system (temperatures, pressures, and voltages). The construction of the test stands differed in detail but provided similar functionality. In contrast to single-cell testing, the AS-SOFC stack was fueled in operando by syngas from a gasifier.

Single-Cell Testing
In the present work, custom-made planar AS-SOFCs (50 × 50 × 1 mm, 16 cm 2 active area) produced at the Institute of Power Engineering, Ceramic Department CEREL were used in the experimental analysis for single-cell testing [44,45]. A cross-section of the cell is shown in Figure 2 together with definitions of particular layers. Alumina housing was used in the experiments. The cells were placed between two gold current collectors. A schematic diagram of the complete test stand is shown in Figure 3. Alumina housing was used in the experiments. The cells were placed between two gold current collectors. A schematic diagram of the complete test stand is shown in Figure 3. The furnace temperature during experimental characterization of single cells was constant at 750 ± 1 °C. Initially, internal reforming in the cell was analyzed in terms of carbon deposition occurring due to the insufficient amount of steam in relation to the fuel supplied. The flow of pure methane (50 Nml/min, methane 5.0, Messer, Poland) was initially humidified at 88 °C using a Cellkraft P-10 humidifier, before entering the fuel cell housing. During the experiment, the steam-to-carbon ratio was gradually decreased from 2.0 to 0.15 by decreasing the humidification temperature, with a step change of approximately 0.1. This approach is equivalent to a situation in which the steam delivering module underperforms, the fuel flow control fails, or a steam leakage occurs. As a result, less H2O is mixed with the fuel. The current load was set at a constant level of 2A for the whole test, which lasted 1000 h. The degradation of the cell was monitored on-line and additionally using electrochemical impedance spectroscopy (EIS), while postmortem analysis was done using a scanning electron microscope, JEOL JSM-6010PLUS/LA (SEM).Additionally a different hypothesis, stating that fuel gas velocity might also affect the carbon deposition process, was analyzed in parallel to the first tests of the experimental campaign. In these cases, constant gas composition of the anodic inlet gas was composed of 12.5% H2, 37.5% CO, and 50% N2, without any addition of steam. Knowing the geometry of the gas channels in the housing and the composition and flow of the fuel, its initial velocity could be calculated. In the performed experiments, anodic gas flow in the range from 120 NmL/min to 640 NmL/min, corresponding to 0.1 m/s and 0.7 m/s, respectively, was analyzed experimentally. Six independent tests were performed-three runs at constant current 3A and an additional three experiments in open circuit voltage conditions. Excluding cell reduction, heating and cooling, the observation of cell performance was conducted for 7 h of measurements per case. This length allowed clear observation of carbon deposition in both in operando measurements as well as postmortem samples. For each experiment, EIS measurements were performed in order to determine SOFC degradation over time under constant electric load.
Additionally, after completing the experimental campaign, the last test with a single cell was realized. It aimed to monitor cell performance degradation in the same conditions, but for 200 h instead of 7 h.

Stack Testing
The analysis of carbon deposition in the 5-cell stack was done using custom-made anodesupported cells composed of the following layers: Ni-YSZ|YSZ|GDC|LSC. The stack was composed of interconnects made of ferritic stainless steel with composite glass seals which were manufactured and assembled in SOFC/SOE stack production facilities of CTH2. The fueling gas was produced in the gasifier, in a similar manner to that presented by Subotic V., et al. [46]. The furnace temperature during experimental characterization of single cells was constant at 750 ± 1 • C. Initially, internal reforming in the cell was analyzed in terms of carbon deposition occurring due to the insufficient amount of steam in relation to the fuel supplied. The flow of pure methane (50 Nml/min, methane 5.0, Messer, Poland) was initially humidified at 88 • C using a Cellkraft P-10 humidifier, before entering the fuel cell housing. During the experiment, the steam-to-carbon ratio was gradually decreased from 2.0 to 0.15 by decreasing the humidification temperature, with a step change of approximately 0.1. This approach is equivalent to a situation in which the steam delivering module underperforms, the fuel flow control fails, or a steam leakage occurs. As a result, less H 2 O is mixed with the fuel. The current load was set at a constant level of 2A for the whole test, which lasted 1000 h. The degradation of the cell was monitored on-line and additionally using electrochemical impedance spectroscopy (EIS), while postmortem analysis was done using a scanning electron microscope, JEOL JSM-6010PLUS/LA (SEM).
Additionally a different hypothesis, stating that fuel gas velocity might also affect the carbon deposition process, was analyzed in parallel to the first tests of the experimental campaign. In these cases, constant gas composition of the anodic inlet gas was composed of 12.5% H 2 , 37.5% CO, and 50% N 2 , without any addition of steam. Knowing the geometry of the gas channels in the housing and the composition and flow of the fuel, its initial velocity could be calculated. In the performed experiments, anodic gas flow in the range from 120 NmL/min to 640 NmL/min, corresponding to 0.1 m/s and 0.7 m/s, respectively, was analyzed experimentally. Six independent tests were performed-three runs at constant current 3A and an additional three experiments in open circuit voltage conditions. Excluding cell reduction, heating and cooling, the observation of cell performance was conducted for 7 h of measurements per case. This length allowed clear observation of carbon deposition in both in operando measurements as well as postmortem samples. For each experiment, EIS measurements were performed in order to determine SOFC degradation over time under constant electric load.
Additionally, after completing the experimental campaign, the last test with a single cell was realized. It aimed to monitor cell performance degradation in the same conditions, but for 200 h instead of 7 h.

Stack Testing
The analysis of carbon deposition in the 5-cell stack was done using custom-made anode-supported cells composed of the following layers: Ni-YSZ|YSZ|GDC|LSC. The stack was composed of interconnects made of ferritic stainless steel with composite glass seals which were manufactured and assembled in SOFC/SOE stack production facilities of CTH 2 . The fueling gas was produced in the gasifier, in a similar manner to that presented by Subotic V., et al. [46].
The gasification system included a buffer tank for the feedstock, a screw feeder, the KAJOT gasification reactor [47], a cyclone-based separator of fine particles installed downstream of the gasifier, a heat exchanger of flue gas, and fans for continuous gas supply. Volatile matter, released from the feedstock in the pyrolysis step, was burned in the first section. Combustion reactions were exothermic and the heat generated during this step was delivered to the drying/pyrolysis stage and to the gasification zone in order to sustain the endothermic gasification reactions.
In the test the feedstock was common hardwood wood chips composed of an alder and beech mixture in a 50/50 ratio. The dimensions of the wood chips were ca. 10 × 10 × 3 mm. In the experiment air was used as a gasifying agent. The volatile matter released from the heated-up feedstock burns in a separate chamber in the reactor and the flue gases produced heat up the gasifying agent through a heat exchanger. In the second zone the main process of gasification takes place. The gas generated is composed mainly of flammable gases CO, H 2 , CO 2 , CH 4 , N 2 used as an inert gas, and H 2 O. However, the gasification product gas contains trace amounts of other contaminants such as particles, tars, and sulfur compounds in the form of H 2 S and COS. The type and amount of contaminants relate to the type of biomass feedstock, temperature of the process, gasifying agent, residence time, equivalence ratio, and type of gasifier [48]. A cyclone was installed downstream of the reactor to separate solid particles from the gas. During the experiment, average fuel flow was 9.49 kg/h and average cold gas efficiency (CGE) was 68.5%. A small part of the gas was transported through a heated (200 • C) line to the SOFC stack. The main part of the gas stream was burned in a separate combustion chamber. A schematic diagram of connection is presented in Figure 4.
Processes 2020, 8, x FOR PEER REVIEW 6 of 21 The gasification system included a buffer tank for the feedstock, a screw feeder, the KAJOT gasification reactor [47], a cyclone-based separator of fine particles installed downstream of the gasifier, a heat exchanger of flue gas, and fans for continuous gas supply. Volatile matter, released from the feedstock in the pyrolysis step, was burned in the first section. Combustion reactions were exothermic and the heat generated during this step was delivered to the drying/pyrolysis stage and to the gasification zone in order to sustain the endothermic gasification reactions.
In the test the feedstock was common hardwood wood chips composed of an alder and beech mixture in a 50/50 ratio. The dimensions of the wood chips were ca. 10 × 10 × 3 mm. In the experiment air was used as a gasifying agent. The volatile matter released from the heated-up feedstock burns in a separate chamber in the reactor and the flue gases produced heat up the gasifying agent through a heat exchanger. In the second zone the main process of gasification takes place. The gas generated is composed mainly of flammable gases CO, H2, CO2, CH4, N2 used as an inert gas, and H2O. However, the gasification product gas contains trace amounts of other contaminants such as particles, tars, and sulfur compounds in the form of H2S and COS. The type and amount of contaminants relate to the type of biomass feedstock, temperature of the process, gasifying agent, residence time, equivalence ratio, and type of gasifier [48]. A cyclone was installed downstream of the reactor to separate solid particles from the gas. During the experiment, average fuel flow was 9.49 kg/h and average cold gas efficiency (CGE) was 68.5%. A small part of the gas was transported through a heated (200 °C) line to the SOFC stack. The main part of the gas stream was burned in a separate combustion chamber. A schematic diagram of connection is presented in Figure 4. The stack was operated in a test stand consisting of an electric oven, gas analyzers, electrochemical workstation (Zahner IM6ex+PP240-used for selected cell EIS measurements), electronic load Chroma 6310A, and data acquisition system (temperatures, pressures, and voltages). The test setup scheme is presented in Figure 5. The stack was operated in a test stand consisting of an electric oven, gas analyzers, electrochemical workstation (Zahner IM6ex+PP240-used for selected cell EIS measurements), electronic load Chroma 6310A, and data acquisition system (temperatures, pressures, and voltages). The test setup scheme is presented in Figure 5.
During the first heat up, the stack was compressed at elevated temperature in order to obtain gas-tightness. Then the procedure to reduce nickel oxide was initiated. This stage of experiment was performed with reference fuel, which is a mixture of hydrogen and nitrogen. After conducting the initial measurements of stack performance and verifying gas-tightness, the stack fuel source was switched from the hydrogen/nitrogen mixture to the gasification product gas from the KAJOT gasifier. The air flow through the stack was kept constant at 10 Nl/min throughout the whole test run. During the first heat up, the stack was compressed at elevated temperature in order to obtain gas-tightness. Then the procedure to reduce nickel oxide was initiated. This stage of experiment was performed with reference fuel, which is a mixture of hydrogen and nitrogen. After conducting the initial measurements of stack performance and verifying gas-tightness, the stack fuel source was switched from the hydrogen/nitrogen mixture to the gasification product gas from the KAJOT gasifier. The air flow through the stack was kept constant at 10 Nl/min throughout the whole test run.
The experiment was conducted under constant current load, which was initially set at 25 A, but after a few hours of operation the load was decreased to 20 A and remained constant to the end of the experiment. During the test, stack temperature was kept constant at 680 °C with variations of +/− 0.5 °C.
The flow of fuel has been maintained with a high temperature pump operated at 180 °C equipped with a manual control valve. Regulation of the flow was done periodically, every 120 min with a manual flowmeter at the stack outlet to keep the fuel utilization (FU) coefficient at a constant 8%. The flow was maintained at 3 ÷ 3.5 Nl/min depending on the content of hydrogen, carbon monoxide, and methane in the producer gas. It is important to note that while no significant fluctuations of the flow were observed throughout the one-week test campaign, the composition of gas fluctuated slightly and therefore the flow had to be adjusted to keep the FU unchanged.

Single SOFC
Numerous EIS measurements were performed during the 1000 h test with decreasing amounts of steam delivered. A reference sample of measured spectrum for a steam-to-carbon ratio of 0.88 is shown in Figure 6. The EIS comparison for different S/C ratio values is shown in Figure 7. The experiment was conducted under constant current load, which was initially set at 25 A, but after a few hours of operation the load was decreased to 20 A and remained constant to the end of the experiment. During the test, stack temperature was kept constant at 680 • C with variations of The flow of fuel has been maintained with a high temperature pump operated at 180 • C equipped with a manual control valve. Regulation of the flow was done periodically, every 120 min with a manual flowmeter at the stack outlet to keep the fuel utilization (FU) coefficient at a constant 8%. The flow was maintained at 3 ÷ 3.5 Nl/min depending on the content of hydrogen, carbon monoxide, and methane in the producer gas. It is important to note that while no significant fluctuations of the flow were observed throughout the one-week test campaign, the composition of gas fluctuated slightly and therefore the flow had to be adjusted to keep the FU unchanged.

Single SOFC
Numerous EIS measurements were performed during the 1000 h test with decreasing amounts of steam delivered. A reference sample of measured spectrum for a steam-to-carbon ratio of 0.88 is shown in Figure 6. The EIS comparison for different S/C ratio values is shown in Figure 7. The collected data shows that the decrease in S/C was followed by an increase in the resistance of the fuel cell, but without the qualitative changes in the impedance pattern. These changes can be described as two RQ arcs with RL chain in high frequencies (similar to those presented in [49]). For the realized EIS, both ohmic cell resistance and cell area-specific resistance (ASR) were determined. For the performed spectroscopy measurements on the SOFC, resistance values below 10 Hz were distorted, as shown in Figure 6. As a result, it was difficult to accurately determine the actual area specific resistance, but it can be assumed that cell ASR was similar in each case. Observed distortions on low frequencies were caused by several processes occurring simultaneously in the anodic compartments of the SOFC including partial direct steam reforming (highly endothermic), electrochemical oxidation (highly exothermic), and formation of carbon particles. Similar effects were observed by Subotic et al. [50]. With each drop of S/C value, ohmic cell resistance of the SOFC increased, thus showing the undesirable changes in cell structure. The correlation between DC cell ohmic resistance (referred to as R1), ASR, and steam-to-carbon ratio is presented in Figure 8. The collected data shows that the decrease in S/C was followed by an increase in the resistance of the fuel cell, but without the qualitative changes in the impedance pattern. These changes can be described as two RQ arcs with RL chain in high frequencies (similar to those presented in [49]). For the realized EIS, both ohmic cell resistance and cell area-specific resistance (ASR) were determined. For the performed spectroscopy measurements on the SOFC, resistance values below 10 Hz were distorted, as shown in Figure 6. As a result, it was difficult to accurately determine the actual area specific resistance, but it can be assumed that cell ASR was similar in each case. Observed distortions on low frequencies were caused by several processes occurring simultaneously in the anodic compartments of the SOFC including partial direct steam reforming (highly endothermic), electrochemical oxidation (highly exothermic), and formation of carbon particles. Similar effects were observed by Subotic et al. [50]. With each drop of S/C value, ohmic cell resistance of the SOFC increased, thus showing the undesirable changes in cell structure. The correlation between DC cell ohmic resistance (referred to as R1), ASR, and steam-to-carbon ratio is presented in Figure 8. The collected data shows that the decrease in S/C was followed by an increase in the resistance of the fuel cell, but without the qualitative changes in the impedance pattern. These changes can be described as two RQ arcs with RL chain in high frequencies (similar to those presented in [49]).
For the realized EIS, both ohmic cell resistance and cell area-specific resistance (ASR) were determined. For the performed spectroscopy measurements on the SOFC, resistance values below 10 Hz were distorted, as shown in Figure 6. As a result, it was difficult to accurately determine the actual area specific resistance, but it can be assumed that cell ASR was similar in each case. Observed distortions on low frequencies were caused by several processes occurring simultaneously in the anodic compartments of the SOFC including partial direct steam reforming (highly endothermic), electrochemical oxidation (highly exothermic), and formation of carbon particles. Similar effects were observed by Subotic et al. [50]. With each drop of S/C value, ohmic cell resistance of the SOFC increased, thus showing the undesirable changes in cell structure. The correlation between DC cell ohmic resistance (referred to as R1), ASR, and steam-to-carbon ratio is presented in Figure 8. During the 1000 h-long experiment, cell voltage was also measured. It is presented in Figure 9. Additionally, both cell resistance and steam-to-carbon ratio were also presented in the graph. The major voltage drop of around 240 h was caused by the change of electric load from 1 A to 2 A, due to the fact that for smaller current, cell was operating in the activation area. Initially, with lower amount of steam, cell performance was better, caused by the less-diluted fuel delivered to the cell. Eventually, voltage drop started when S/C was equal to 0.88, resulting in damaging the cell, which was also observed by a significant increase of cell resistance. Further lowering the steam-to-carbon ratio caused accelerated cell performance degradation. During the 1000 h-long experiment, cell voltage was also measured. It is presented in Figure 9. During the 1000 h-long experiment, cell voltage was also measured. It is presented in Figure 9. Additionally, both cell resistance and steam-to-carbon ratio were also presented in the graph. The major voltage drop of around 240 h was caused by the change of electric load from 1 A to 2 A, due to the fact that for smaller current, cell was operating in the activation area. Initially, with lower amount of steam, cell performance was better, caused by the less-diluted fuel delivered to the cell. Eventually, voltage drop started when S/C was equal to 0.88, resulting in damaging the cell, which was also observed by a significant increase of cell resistance. Further lowering the steam-to-carbon ratio caused accelerated cell performance degradation. Additionally, both cell resistance and steam-to-carbon ratio were also presented in the graph. The major voltage drop of around 240 h was caused by the change of electric load from 1 A to 2 A, due to the fact that for smaller current, cell was operating in the activation area. Initially, with lower amount of steam, cell performance was better, caused by the less-diluted fuel delivered to the cell. Eventually, voltage drop started when S/C was equal to 0.88, resulting in damaging the cell, which was also observed by a significant increase of cell resistance. Further lowering the steam-to-carbon ratio caused accelerated cell performance degradation.
With a lower amount of steam delivered, a bigger role was taken by the soot-formation reactions-a lower S/C ratio results in the deflection of the equilibrium of the Boudouard reaction (Equation (6)) in favor of carbon deposition and increased activity of the carbon monoxide (according to Equation (3)). Also steam oxidation of the carbon deposits (Equation (5)), including nucleuses of the solid phase, becomes more unlikely. Boundary values for S/C can be found on Figure 1. The postmortem analysis showed that at low S/C conditions serious cracks occurred near the fuel inlet during the test. Likely it is a synergetic effect of the thermal stresses, induced by endothermic steam conversion of the methane (Equation (1)) and growth of the carbon deposits on the anode support. It is necessary to mention here that more prominent evidence of the cell destruction were observed on the cathode side, due to leakage of the fuel through cracks in the cathode compartment, which led to delamination of the Lanthanum Strontium Cobalt Ferrite (LSCF) layer. However, SEM analysis demonstrated existence of the dense net of the crack in the anode support. Only the biggest of these cracks is likely to reach the cathodic side of the cell. Figure 10 presents the state of the SOFC near the fuel inlet after the 1000-h experiment with decreasing S/C ratio.
With a lower amount of steam delivered, a bigger role was taken by the soot-formation reactions-a lower S/C ratio results in the deflection of the equilibrium of the Boudouard reaction (Equation (6)) in favor of carbon deposition and increased activity of the carbon monoxide (according to Equation (3)). Also steam oxidation of the carbon deposits (Equation (5)), including nucleuses of the solid phase, becomes more unlikely. Boundary values for S/C can be found on Figure 1. The postmortem analysis showed that at low S/C conditions serious cracks occurred near the fuel inlet during the test. Likely it is a synergetic effect of the thermal stresses, induced by endothermic steam conversion of the methane (Equation (1)) and growth of the carbon deposits on the anode support. It is necessary to mention here that more prominent evidence of the cell destruction were observed on the cathode side, due to leakage of the fuel through cracks in the cathode compartment, which led to delamination of the Lanthanum Strontium Cobalt Ferrite (LSCF) layer. However, SEM analysis demonstrated existence of the dense net of the crack in the anode support. Only the biggest of these cracks is likely to reach the cathodic side of the cell. Figure 10 presents the state of the SOFC near the fuel inlet after the 1000-h experiment with decreasing S/C ratio. For the experiments with simulated reformate at different velocities, postmortem observations are shown in Table 1. For the experiments with simulated reformate at different velocities, postmortem observations are shown in Table 1. With a lower amount of steam delivered, a bigger role was taken by the soot-formation reactions-a lower S/C ratio results in the deflection of the equilibrium of the Boudouard reaction (Equation (6)) in favor of carbon deposition and increased activity of the carbon monoxide (according to Equation (3)). Also steam oxidation of the carbon deposits (Equation (5)), including nucleuses of the solid phase, becomes more unlikely. Boundary values for S/C can be found on Figure 1. The postmortem analysis showed that at low S/C conditions serious cracks occurred near the fuel inlet during the test. Likely it is a synergetic effect of the thermal stresses, induced by endothermic steam conversion of the methane (Equation (1)) and growth of the carbon deposits on the anode support. It is necessary to mention here that more prominent evidence of the cell destruction were observed on the cathode side, due to leakage of the fuel through cracks in the cathode compartment, which led to delamination of the Lanthanum Strontium Cobalt Ferrite (LSCF) layer. However, SEM analysis demonstrated existence of the dense net of the crack in the anode support. Only the biggest of these cracks is likely to reach the cathodic side of the cell. Figure 10 presents the state of the SOFC near the fuel inlet after the 1000-h experiment with decreasing S/C ratio. For the experiments with simulated reformate at different velocities, postmortem observations are shown in Table 1. With a lower amount of steam delivered, a bigger role was taken by the soot-formation reactions-a lower S/C ratio results in the deflection of the equilibrium of the Boudouard reaction (Equation (6)) in favor of carbon deposition and increased activity of the carbon monoxide (according to Equation (3)). Also steam oxidation of the carbon deposits (Equation (5)), including nucleuses of the solid phase, becomes more unlikely. Boundary values for S/C can be found on Figure 1. The postmortem analysis showed that at low S/C conditions serious cracks occurred near the fuel inlet during the test. Likely it is a synergetic effect of the thermal stresses, induced by endothermic steam conversion of the methane (Equation (1)) and growth of the carbon deposits on the anode support. It is necessary to mention here that more prominent evidence of the cell destruction were observed on the cathode side, due to leakage of the fuel through cracks in the cathode compartment, which led to delamination of the Lanthanum Strontium Cobalt Ferrite (LSCF) layer. However, SEM analysis demonstrated existence of the dense net of the crack in the anode support. Only the biggest of these cracks is likely to reach the cathodic side of the cell. Figure 10 presents the state of the SOFC near the fuel inlet after the 1000-h experiment with decreasing S/C ratio. For the experiments with simulated reformate at different velocities, postmortem observations are shown in Table 1. With a lower amount of steam delivered, a bigger role was taken by the soot-formation reactions-a lower S/C ratio results in the deflection of the equilibrium of the Boudouard reaction (Equation (6)) in favor of carbon deposition and increased activity of the carbon monoxide (according to Equation (3)). Also steam oxidation of the carbon deposits (Equation (5)), including nucleuses of the solid phase, becomes more unlikely. Boundary values for S/C can be found on Figure 1. The postmortem analysis showed that at low S/C conditions serious cracks occurred near the fuel inlet during the test. Likely it is a synergetic effect of the thermal stresses, induced by endothermic steam conversion of the methane (Equation (1)) and growth of the carbon deposits on the anode support. It is necessary to mention here that more prominent evidence of the cell destruction were observed on the cathode side, due to leakage of the fuel through cracks in the cathode compartment, which led to delamination of the Lanthanum Strontium Cobalt Ferrite (LSCF) layer. However, SEM analysis demonstrated existence of the dense net of the crack in the anode support. Only the biggest of these cracks is likely to reach the cathodic side of the cell. Figure 10 presents the state of the SOFC near the fuel inlet after the 1000-h experiment with decreasing S/C ratio. For the experiments with simulated reformate at different velocities, postmortem observations are shown in Table 1.  The results obtained prove that gas velocity correlates with the carbon deposition process. When the SOFC works in OCV conditions, formation of carbon solid particles is more intense than when it operates under current load. As a result, a low amount of steam and a high concentration of CO favors the decomposition of CO in the Boudouard process (Equation (6)).
The results for the extended test (200 h) are shown in Figure 11. The initial time corresponds to the start of carbon deposition. Initially, the experiments were performed for 0.7 m/s initial, anodic gas velocity. As presented in Figure 11, it was observed that fuel cell electrochemical performance was highly dependent on the carbon deposition process. During the first 24 h of operation after the switch of fuel from H2-N2 to the CO-H2-N2 mixture, degradation was minor and was observable only by some evolution of EIS spectra and minor decrease in voltage equals ca. 4.3 mV. In the next phase, the transition process occurred and led to a significant drop in voltage. The duration of transition was approximately 48 h, during which the resistances that may be attributed to the electrochemical processes increased (including cathodic), resulting in the increase of ASR of the cell from ca. 0.34 Ω × cm 2 at the beginning of the experiment up to ca. 0.6 Ω × cm 2 at its termination. Simultaneously the ohmic resistance fell slightly from ca. 0.38 Ω × cm 2 (initially) down to ca. 0.33 Ω × cm 2 . The latter phenomenon may be explained as enhancement of the contact between anode and the current collector due to deposition of carbon particles which exhibit good conductivity. Similar phenomena were to some extent observed by Lyu et al. [36]. The rise in cathodic polarization may be explained through the exclusion of the soot-covered area of the cell from transport of electric current. Slow degradation was observable even after 162 h of operation.
The complex nature of the observed phenomena (anode degradation, blocking of the cell surface from charge transportation, etc.) meant that we were unable to create a tolerable model for equivalent The results obtained prove that gas velocity correlates with the carbon deposition process. When the SOFC works in OCV conditions, formation of carbon solid particles is more intense than when it operates under current load. As a result, a low amount of steam and a high concentration of CO favors the decomposition of CO in the Boudouard process (Equation (6)).
The results for the extended test (200 h) are shown in Figure 11. The initial time corresponds to the start of carbon deposition. Initially, the experiments were performed for 0.7 m/s initial, anodic gas velocity. As presented in Figure 11, it was observed that fuel cell electrochemical performance was highly dependent on the carbon deposition process. During the first 24 h of operation after the switch of fuel from H2-N2 to the CO-H2-N2 mixture, degradation was minor and was observable only by some evolution of EIS spectra and minor decrease in voltage equals ca. 4.3 mV. In the next phase, the transition process occurred and led to a significant drop in voltage. The duration of transition was approximately 48 h, during which the resistances that may be attributed to the electrochemical processes increased (including cathodic), resulting in the increase of ASR of the cell from ca. 0.34 Ω × cm 2 at the beginning of the experiment up to ca. 0.6 Ω × cm 2 at its termination. Simultaneously the ohmic resistance fell slightly from ca. 0.38 Ω × cm 2 (initially) down to ca. 0.33 Ω × cm 2 . The latter phenomenon may be explained as enhancement of the contact between anode and the current collector due to deposition of carbon particles which exhibit good conductivity. Similar phenomena were to some extent observed by Lyu et al. [36]. The rise in cathodic polarization may be explained through the exclusion of the soot-covered area of the cell from transport of electric current. Slow degradation was observable even after 162 h of operation.
The complex nature of the observed phenomena (anode degradation, blocking of the cell surface from charge transportation, etc.) meant that we were unable to create a tolerable model for equivalent The results obtained prove that gas velocity correlates with the carbon deposition process. When the SOFC works in OCV conditions, formation of carbon solid particles is more intense than when it operates under current load. As a result, a low amount of steam and a high concentration of CO favors the decomposition of CO in the Boudouard process (Equation (6)).
The results for the extended test (200 h) are shown in Figure 11. The initial time corresponds to the start of carbon deposition. Initially, the experiments were performed for 0.7 m/s initial, anodic gas velocity. As presented in Figure 11, it was observed that fuel cell electrochemical performance was highly dependent on the carbon deposition process. During the first 24 h of operation after the switch of fuel from H2-N2 to the CO-H2-N2 mixture, degradation was minor and was observable only by some evolution of EIS spectra and minor decrease in voltage equals ca. 4.3 mV. In the next phase, the transition process occurred and led to a significant drop in voltage. The duration of transition was approximately 48 h, during which the resistances that may be attributed to the electrochemical processes increased (including cathodic), resulting in the increase of ASR of the cell from ca. 0.34 Ω × cm 2 at the beginning of the experiment up to ca. 0.6 Ω × cm 2 at its termination. Simultaneously the ohmic resistance fell slightly from ca. 0.38 Ω × cm 2 (initially) down to ca. 0.33 Ω × cm 2 . The latter phenomenon may be explained as enhancement of the contact between anode and the current collector due to deposition of carbon particles which exhibit good conductivity. Similar phenomena were to some extent observed by Lyu et al. [36]. The rise in cathodic polarization may be explained through the exclusion of the soot-covered area of the cell from transport of electric current. Slow degradation was observable even after 162 h of operation.
The complex nature of the observed phenomena (anode degradation, blocking of the cell surface from charge transportation, etc.) meant that we were unable to create a tolerable model for equivalent The results obtained prove that gas velocity correlates with the carbon deposition process. When the SOFC works in OCV conditions, formation of carbon solid particles is more intense than when it operates under current load. As a result, a low amount of steam and a high concentration of CO favors the decomposition of CO in the Boudouard process (Equation (6)).
The results for the extended test (200 h) are shown in Figure 11. The initial time corresponds to the start of carbon deposition. Initially, the experiments were performed for 0.7 m/s initial, anodic gas velocity. The results obtained prove that gas velocity correlates with the carbon deposition process. When the SOFC works in OCV conditions, formation of carbon solid particles is more intense than when it operates under current load. As a result, a low amount of steam and a high concentration of CO favors the decomposition of CO in the Boudouard process (Equation (6)).
The results for the extended test (200 h) are shown in Figure 11. The initial time corresponds to the start of carbon deposition. Initially, the experiments were performed for 0.7 m/s initial, anodic gas velocity. As presented in Figure 11, it was observed that fuel cell electrochemical performance was highly dependent on the carbon deposition process. During the first 24 h of operation after the switch of fuel from H2-N2 to the CO-H2-N2 mixture, degradation was minor and was observable only by some evolution of EIS spectra and minor decrease in voltage equals ca. 4.3 mV. In the next phase, the transition process occurred and led to a significant drop in voltage. The duration of transition was approximately 48 h, during which the resistances that may be attributed to the electrochemical processes increased (including cathodic), resulting in the increase of ASR of the cell from ca. 0.34 Ω × cm 2 at the beginning of the experiment up to ca. 0.6 Ω × cm 2 at its termination. Simultaneously the ohmic resistance fell slightly from ca. 0.38 Ω × cm 2 (initially) down to ca. 0.33 Ω × cm 2 . The latter phenomenon may be explained as enhancement of the contact between anode and the current collector due to deposition of carbon particles which exhibit good conductivity. Similar phenomena were to some extent observed by Lyu et al. [36]. The rise in cathodic polarization may be explained through the exclusion of the soot-covered area of the cell from transport of electric current. Slow degradation was observable even after 162 h of operation.
The complex nature of the observed phenomena (anode degradation, blocking of the cell surface from charge transportation, etc.) meant that we were unable to create a tolerable model for equivalent Figure 11. Impact of soot formation on fuel cell degradation-selected results of the EIS measurements. Data recorder under initial gas velocity of 0.7 m/s at 750 • C, amplitude 10 mV.
As presented in Figure 11, it was observed that fuel cell electrochemical performance was highly dependent on the carbon deposition process. During the first 24 h of operation after the switch of fuel from H 2 -N 2 to the CO-H 2 -N 2 mixture, degradation was minor and was observable only by some evolution of EIS spectra and minor decrease in voltage equals ca. 4.3 mV. In the next phase, the transition process occurred and led to a significant drop in voltage. The duration of transition was approximately 48 h, during which the resistances that may be attributed to the electrochemical processes increased (including cathodic), resulting in the increase of ASR of the cell from ca. 0.34 Ω × cm 2 at the beginning of the experiment up to ca. 0.6 Ω × cm 2 at its termination. Simultaneously the ohmic resistance fell slightly from ca. 0.38 Ω × cm 2 (initially) down to ca. 0.33 Ω × cm 2 . The latter phenomenon may be explained as enhancement of the contact between anode and the current collector due to deposition of carbon particles which exhibit good conductivity. Similar phenomena were to some extent observed by Lyu et al. [36]. The rise in cathodic polarization may be explained through the exclusion of the soot-covered area of the cell from transport of electric current. Slow degradation was observable even after 162 h of operation.
The complex nature of the observed phenomena (anode degradation, blocking of the cell surface from charge transportation, etc.) meant that we were unable to create a tolerable model for equivalent circuits to describe the evolution of the impedance spectra. The degradation of the fuel cell caused by carbon deposition can be divided into three characteristic zones, as presented in Figure 12.
Processes 2020, 8, x FOR PEER REVIEW 12 of 21 circuits to describe the evolution of the impedance spectra. The degradation of the fuel cell caused by carbon deposition can be divided into three characteristic zones, as presented in Figure 12. In Zone 1 approximately 23-24 h degradation of ca. 180 mV/1000 h was observed. The most aggressive degradation appeared in Zone 2, where the voltage dropped by ca. 120 mV in less than 48 h. The degradation rate in Zone 3 was similar to Zone 1, with a low degradation rate of ca. 170 mV/1000 h. It can be concluded that the carbon formation and deposition process started at the beginning of Zone 2. After solid carbon particles blocked the pores of the anode, there was no further observable impact of soot deposition on fuel cell performance and a return to slow degradation ensued in Zone 3.
The same analysis was performed for the other initial fuel velocity values: 0.3 m/s and 0.5 m/s. Both values of OCV and cell voltage at 3 A load were different for each anode gas velocity case, thus a different approach was proposed for comparison purposes. In Figure 13, voltage drops were shown with reference to the initial value of each experiment. The dots in the chart represent the actual voltage drop measurements, while the thin lines are approximations for visualization purposes only.  In Zone 1 approximately 23-24 h degradation of ca. 180 mV/1000 h was observed. The most aggressive degradation appeared in Zone 2, where the voltage dropped by ca. 120 mV in less than 48 h. The degradation rate in Zone 3 was similar to Zone 1, with a low degradation rate of ca. 170 mV/1000 h. It can be concluded that the carbon formation and deposition process started at the beginning of Zone 2. After solid carbon particles blocked the pores of the anode, there was no further observable impact of soot deposition on fuel cell performance and a return to slow degradation ensued in Zone 3.
The same analysis was performed for the other initial fuel velocity values: 0.3 m/s and 0.5 m/s. Both values of OCV and cell voltage at 3 A load were different for each anode gas velocity case, thus a different approach was proposed for comparison purposes. In Figure 13, voltage drops were shown with reference to the initial value of each experiment. The dots in the chart represent the actual voltage drop measurements, while the thin lines are approximations for visualization purposes only. circuits to describe the evolution of the impedance spectra. The degradation of the fuel cell caused by carbon deposition can be divided into three characteristic zones, as presented in Figure 12. In Zone 1 approximately 23-24 h degradation of ca. 180 mV/1000 h was observed. The most aggressive degradation appeared in Zone 2, where the voltage dropped by ca. 120 mV in less than 48 h. The degradation rate in Zone 3 was similar to Zone 1, with a low degradation rate of ca. 170 mV/1000 h. It can be concluded that the carbon formation and deposition process started at the beginning of Zone 2. After solid carbon particles blocked the pores of the anode, there was no further observable impact of soot deposition on fuel cell performance and a return to slow degradation ensued in Zone 3.
The same analysis was performed for the other initial fuel velocity values: 0.3 m/s and 0.5 m/s. Both values of OCV and cell voltage at 3 A load were different for each anode gas velocity case, thus a different approach was proposed for comparison purposes. In Figure 13, voltage drops were shown with reference to the initial value of each experiment. The dots in the chart represent the actual voltage drop measurements, while the thin lines are approximations for visualization purposes only.  Based on the analysis of the results it can be concluded that a similar degradation rate was observed during each of the experiments. Taking into account the measurements, the time after the fuel cell that rapid degradation begins (transition from Zone 1 to 2) can be correlated with the anode gas velocity according to: where t cd is time elapsed after which the rapid fuel cell degradation caused by carbon deposition starts and v is the anodic gas velocity. Because the high anode thickness (1 mm) clearly damps the dynamics of performance degradation, the formula might be amended by factoring in the thickness of the anode.

SOFC Stack
Before fueling the SOFC stack with producer gas from a prototype, two-section, downdraft gasifier, KAJOT, the initial stack performance was measured. The reference curve was obtained for the hydrogen/nitrogen mixture ( Figure 14). Power density at 0.9 V was~0.275 W/cm 2 and cell ASR calculated from the I-V curve between 0.9 and 0.85 V for a representative fuel cell in the stack (no 3) was 0.36 Ω × cm 2 . Based on the analysis of the results it can be concluded that a similar degradation rate was observed during each of the experiments. Taking into account the measurements, the time after the fuel cell that rapid degradation begins (transition from Zone 1 to 2) can be correlated with the anode gas velocity according to: = −37.5 + 90 − 20.625 (7) where tcd is time elapsed after which the rapid fuel cell degradation caused by carbon deposition starts and v is the anodic gas velocity. Because the high anode thickness (1 mm) clearly damps the dynamics of performance degradation, the formula might be amended by factoring in the thickness of the anode.

SOFC Stack
Before fueling the SOFC stack with producer gas from a prototype, two-section, downdraft gasifier, KAJOT, the initial stack performance was measured. The reference curve was obtained for the hydrogen/nitrogen mixture ( Figure 14). Power density at 0.9 V was ~0.275 W/cm 2 and cell ASR calculated from the I-V curve between 0.9 and 0.85 V for a representative fuel cell in the stack (no 3) was 0.36 Ω × cm 2 . Afterwards the stack fuel source was switched from the hydrogen/nitrogen mixture to the gasification product gas. Gas composition fluctuated throughout the test. The representative composition of the producer gas together with observed fluctuations is presented in Table 2. Afterwards the stack fuel source was switched from the hydrogen/nitrogen mixture to the gasification product gas. Gas composition fluctuated throughout the test. The representative composition of the producer gas together with observed fluctuations is presented in Table 2. To gain deeper understanding of the fuel composition from the carbon deposition point of view, Gibbs triangle with isotherms of carbon formation was prepared. Average syngas composition was used in order to determine the operating point, which is presented as a red dot in Figure 15. Mathematical calculations proved that the operating temperature (680 • C) together with the wet gas composition (8% water content) was very close to the isotherm which separates the safe operating zone from the operating conditions at which carbon deposition thermodynamically occurs. The test with producer gas was conducted under current load with current density of ca. 0.2 A/cm 2 , equivalent to the one applied in the tests for the 50 mm × 50 mm cells. This produced comparable conditions in terms of the carbon deposition process in both environments-small single cell and the stack fueled by real fuel.  To gain deeper understanding of the fuel composition from the carbon deposition point of view, Gibbs triangle with isotherms of carbon formation was prepared. Average syngas composition was used in order to determine the operating point, which is presented as a red dot in Figure 15. Mathematical calculations proved that the operating temperature (680 °C) together with the wet gas composition (8% water content) was very close to the isotherm which separates the safe operating zone from the operating conditions at which carbon deposition thermodynamically occurs. The test with producer gas was conducted under current load with current density of ca. 0.2 A/cm 2 , equivalent to the one applied in the tests for the 50 mm × 50 mm cells. This produced comparable conditions in terms of the carbon deposition process in both environments-small single cell and the stack fueled by real fuel. During the first 18 h of operation on gasification product gas, the degradation rate was quite low, but later it started to be destructive (ca. 1250 mV/1000 h). Figure 16 demonstrates the loss of performance of a representative cell from the 5-cell stack as a result of operation on the gasificationderived fuel for 120 h. After this period, the stack was cooled and the postmortem analysis phase started. During the first 18 h of operation on gasification product gas, the degradation rate was quite low, but later it started to be destructive (ca. 1250 mV/1000 h). Figure 16 demonstrates the loss of performance of a representative cell from the 5-cell stack as a result of operation on the gasification-derived fuel for 120 h. After this period, the stack was cooled and the postmortem analysis phase started. The investigation proved that an intense carbon deposition process occurred during the test. Figure 17a,b, presenting a view of the anode support edge adjacent to the fuel inlet, demonstrated heavy carbon deposition on the anode of a representative cell. It looked similar in other cells.
Analysis of the experiment data and postmortem results reveal three independent facts impacting the carbon deposition processes: • thermodynamics at least close to the boundary of the heterogenic process, • presence of the catalytical Ni-YSZ SOFC anode, • fluctuations of the gas composition (according to data presented in Table 2).
The dynamic changes in fuel composition shifted the operating conditions beyond the carbon deposition boundary in some parts of the conducted experiment. The results indicate that fuels with carbon-rich compounds are more demanding in system tests and that thermodynamic calculations should definitely take into account their variations as well as the presence of a catalytic anodic surface. In such system design additional steps need to be taken, like further humidification (S:C > 2.2) of fuel in order to extend the safe zone for possible fluctuations in gas composition or operation at higher temperatures. Figure 17 demonstrates the traces of mechanical contact between the steel interconnect and the anode. The visible carbon particles deposited mainly at the inlet of the fuel electrode in areas which were open for flow, between the contact lines. The investigation proved that an intense carbon deposition process occurred during the test. Figure 17a,b, presenting a view of the anode support edge adjacent to the fuel inlet, demonstrated heavy carbon deposition on the anode of a representative cell. It looked similar in other cells.
Analysis of the experiment data and postmortem results reveal three independent facts impacting the carbon deposition processes: • thermodynamics at least close to the boundary of the heterogenic process, • presence of the catalytical Ni-YSZ SOFC anode, • fluctuations of the gas composition (according to data presented in Table 2).
The dynamic changes in fuel composition shifted the operating conditions beyond the carbon deposition boundary in some parts of the conducted experiment. The results indicate that fuels with carbon-rich compounds are more demanding in system tests and that thermodynamic calculations should definitely take into account their variations as well as the presence of a catalytic anodic surface. In such system design additional steps need to be taken, like further humidification (S:C > 2.2) of fuel in order to extend the safe zone for possible fluctuations in gas composition or operation at higher temperatures. Figure 17 demonstrates the traces of mechanical contact between the steel interconnect and the anode. The visible carbon particles deposited mainly at the inlet of the fuel electrode in areas which were open for flow, between the contact lines. The observations of the deposits and the nearby surface were carried out with a Keyence VHS7000 digital microscope, in order to analyze the nature of the visible spots. The images presented in Figure 17c,d show the damage to the nickel contact layer (the outermost layer). The image obtained with no filter (Figure 17c) does not provide a direct answer as to its nature, with a spatial filter and observation from different angles (Figure 17d) it was confirmed that the outer layer was damaged approximately 100 µm deep inside. Some of the deposits were loose, not connected with the surface, and easy to remove from it, while some of them were joined with the surface. The thickness of the latter varied from ca. 50 to 200 µm.
Scanning electron microscopy investigations with Zeiss Ultra Plus equipment were carried out in order to investigate the anode surface in detail and to find out if the carbon deposits occurred elsewhere. Energy Dispersive X-ray method (EDX) was used to identify the elements occurring on the surface. Figure 18a shows the backscattered electron images of the anode support of Ni-8YSZ after disassembly from the stack (postmortem). The shaded black area is the carbon deposition, which was confirmed by the map generated via Energy Dispersive Spectroscopy (EDS) (Figure 18b).
Analysis of the support surface revealed that the carbon particles were deposited not only in the obvious, observed areas near the edge of the cell adjacent to the fuel inlet, but also all over the anode surface. With the SE detector it was possible to determine the microstructure of such micro-deposits of the amorphous carbon (Figure 18c,d)-they consisted of nanometric particles. The observations of the deposits and the nearby surface were carried out with a Keyence VHS7000 digital microscope, in order to analyze the nature of the visible spots. The images presented in Figure 17c,d show the damage to the nickel contact layer (the outermost layer). The image obtained with no filter (Figure 17c) does not provide a direct answer as to its nature, with a spatial filter and observation from different angles (Figure 17d) it was confirmed that the outer layer was damaged approximately 100 µm deep inside. Some of the deposits were loose, not connected with the surface, and easy to remove from it, while some of them were joined with the surface. The thickness of the latter varied from ca. 50 to 200 µm.
Scanning electron microscopy investigations with Zeiss Ultra Plus equipment were carried out in order to investigate the anode surface in detail and to find out if the carbon deposits occurred elsewhere. Energy Dispersive X-ray method (EDX) was used to identify the elements occurring on the surface. Figure 18a shows the backscattered electron images of the anode support of Ni-8YSZ after disassembly from the stack (postmortem). The shaded black area is the carbon deposition, which was confirmed by the map generated via Energy Dispersive Spectroscopy (EDS) (Figure 18b).
Analysis of the support surface revealed that the carbon particles were deposited not only in the obvious, observed areas near the edge of the cell adjacent to the fuel inlet, but also all over the anode surface. With the SE detector it was possible to determine the microstructure of such micro-deposits of the amorphous carbon (Figure 18c,d)-they consisted of nanometric particles.

Comparison of Carbon Contamination for Single-Cell and Stack Environments
As part of this work AS-SOFCs exposed to carbon rich fuel were analyzed in two arrangements: single-cell housing and a 5-cell stack. The single fuel cell was fueled by simulated syngas whereas the AS-SOFC stack was fueled by real syngas produced by the KAJOT two stage gasifier. For the purpose of comparison, tests were performed under constant current load (0.2 A/cm 2 ) and a similar initial velocity profile (0.3 m/s) in gas channels along the anode surface. Due to limitations in the stack construction and test stand, the tests with single cells and stack were performed at 750 °C and 680 °C, respectively.
The AS-SOFCs applied had a similar anode support composition but differed by thickness and active area. The aim of this approach was to demonstrate similarities in the carbon deposition process despite the geometrical differences between the fuel cells. In the case of a 1-mm-thick single cell, the active area was 16 cm 2 . For the stack analysis, five 0.55 mm thick cells, each with 92 cm 2 of active area, were used. Active areas coincided with the screen-printed cathode area.
In Figure 19, voltage drops were shown with reference to the initial velocity in gas channels of the single fuel cell unit and fuel cell stack. Dots in the chart represent the actual voltage drop measurements, while thin lines are approximations for visualization purposes only. Experimental results of stack's fuel cells demonstrate an intensive degradation process (ca. 1250 mV/1000 h) where rapid, transition, and slow degradation zones cannot be distinguished.
In terms of total voltage drop over 80 h, both tests present similarities which can be explained by an analogical amount of deposited carbon within the anode volume. However, except for the total voltage drop, the process character could also be correlated with the different thicknesses of fuel cells.
In the case of anode support that was almost half as thin, the carbon deposition was more detrimental although the total anode volume was almost ten times bigger. In contrast to the thick (1 mm) fuel cell, in the SOFC stack, carbon penetrated the whole volume of the fuel electrodes, also reaching triple phase boundaries (TPB) where electrochemical reactions take place. This explains the inability to separate fast, transition, and slow degradation processes. In the first stage of single fuel cell testing,

Comparison of Carbon Contamination for Single-Cell and Stack Environments
As part of this work AS-SOFCs exposed to carbon rich fuel were analyzed in two arrangements: single-cell housing and a 5-cell stack. The single fuel cell was fueled by simulated syngas whereas the AS-SOFC stack was fueled by real syngas produced by the KAJOT two stage gasifier. For the purpose of comparison, tests were performed under constant current load (0.2 A/cm 2 ) and a similar initial velocity profile (0.3 m/s) in gas channels along the anode surface. Due to limitations in the stack construction and test stand, the tests with single cells and stack were performed at 750 • C and 680 • C, respectively.
The AS-SOFCs applied had a similar anode support composition but differed by thickness and active area. The aim of this approach was to demonstrate similarities in the carbon deposition process despite the geometrical differences between the fuel cells. In the case of a 1-mm-thick single cell, the active area was 16 cm 2 . For the stack analysis, five 0.55 mm thick cells, each with 92 cm 2 of active area, were used. Active areas coincided with the screen-printed cathode area.
In Figure 19, voltage drops were shown with reference to the initial velocity in gas channels of the single fuel cell unit and fuel cell stack. Dots in the chart represent the actual voltage drop measurements, while thin lines are approximations for visualization purposes only. Experimental results of stack's fuel cells demonstrate an intensive degradation process (ca. 1250 mV/1000 h) where rapid, transition, and slow degradation zones cannot be distinguished.
In terms of total voltage drop over 80 h, both tests present similarities which can be explained by an analogical amount of deposited carbon within the anode volume. However, except for the total voltage drop, the process character could also be correlated with the different thicknesses of fuel cells.
In the case of anode support that was almost half as thin, the carbon deposition was more detrimental although the total anode volume was almost ten times bigger. In contrast to the thick (1 mm) fuel cell, in the SOFC stack, carbon penetrated the whole volume of the fuel electrodes, also reaching triple phase boundaries (TPB) where electrochemical reactions take place. This explains the inability to separate fast, transition, and slow degradation processes. In the first stage of single fuel cell testing, carbon deposited mainly on the gas-anode interface (fast degradation). With time it started to penetrate inside the anode (transition zone) until it reached the TPB (slow degradation).
To sum up, the realized experiments revealed a correlation between the thickness of the fuel cells and their operating parameters on the carbon formation process. Dynamic changes in fuel composition shifted the operating conditions to more severe than initially planned. An anode of half the thickness could not compensate for such rapid changes. In such a system even short fluctuations in the syngas composition, especially beyond the thermodynamically-safe zone were enough to trigger the carbon deposition process. As a result, the process was very destructive and comparable to one with the single cell, where operating conditions were more detrimental (in terms of thermodynamics) than in the stack environment. To sum up, the realized experiments revealed a correlation between the thickness of the fuel cells and their operating parameters on the carbon formation process. Dynamic changes in fuel composition shifted the operating conditions to more severe than initially planned. An anode of half the thickness could not compensate for such rapid changes. In such a system even short fluctuations in the syngas composition, especially beyond the thermodynamically-safe zone were enough to trigger the carbon deposition process. As a result, the process was very destructive and comparable to one with the single cell, where operating conditions were more detrimental (in terms of thermodynamics) than in the stack environment.