Fabrication of Lanthanum Strontium Manganite Ceramics via Agar Gel Casting and Solid State Sintering

Fabricating lanthanum strontium manganite (LSM) ceramics with certain shapes is important for the design and construction of high-temperature energy conversion and storage devices. Here, we describe a low-cost and environmentally friendly method for fabricating LSM ceramics via agar gel casting and high temperature sintering. This new approach uses temperature tuning to fabricate LSM gel bodies, not only by manufacturing in the secondary process but also by remolding and recycling during the gel casting process. The effect of the sintering temperature on the properties of LSM ceramics was investigated as well. As a result, the porosity and compressive strength of LSM ceramics sintered at 1000 °C are ~60% and 5.6 MPa, respectively. When the sintering temperature increases to 1200 °C, the porosity decreases to ~28%, whereas the compressive strength increases to 25 MPa, which is able to meet the requirement of cathode-supported SOFCs (solid oxide fuel cells).


Introduction
As a representative of perovskite-type oxide system ceramics, lanthanum strontium manganite (La 1−x Sr x MnO 3 , LSM) attracted intensive interest because of their outstanding electrical conductivity and catalytic activity [1][2][3][4][5], that make them promising cathode materials for high-temperature energy conversion and storage devices, such as solid oxide fuel cells (SOFC) [6][7][8][9] and molten salt batteries [10][11][12]. In particular, forming LSM ceramics is crucial in the design and fabrication of cathode-supported SOFCs [13], which is associated not only with structures and shapes but also with manufacturing costs. Currently, a variety of forming techniques, including dry pressing [14,15], dip coating [7], screen-printing [16], tape casting [17], gel casting [18][19][20] and extrusion molding [21], have been utilized to fabricate porous LSM ceramic electrodes for planar, tubular and honeycomb cathode-supported SOFCs. However, it is still a challenging task for the development of advanced shaping technologies to meet urgent demands of geometrical optimization and cost reduction in the rapidly growing area of cathode-supported SOFCs in micro/meso-scale.
Gel casting is a near-net shape ceramic forming technique that has been widely employed to fabricate electrode-supported substrates for SOFCs [22,23]. Recently, porous LSM cathode tubes in centimeter scale have been fabricated via a typical gel casting process with the binder of polyacrylamide. In order to gelation, many chemicals, i.e., acrylamide, N,N'-methylenebisacrylamide (MBAA),

Materials and Methods
The raw material LSM ceramics with the chemical structure of La 0.65 Sr 0.35 MnO 3 , were purchased from Ningbo SOFCMAN Energy Technology Co., Ltd (Ningbo, China). The LSM nanopowders with the 200-300 nm diameter for gel casting were obtained via ball milling treatment with 4:1 ball-to-powder weight ratio. Agar, polyethylene glycol (PEG-600) and polyacrylic acid (PAA) of 50% aqueous solution were purchased from Aladdin reagent Co., Ltd (Shanghai, China). The ball mill instrument is BMT-30D benchtop ball mill, which was purchased from Hsiangtai Machinery Industry Co., Ltd (New Taipei City, Taiwan). The agar aqueous solution with concentrations of 1 wt%, 2 wt%, 3 wt%, 4 wt%, 5 wt%, respectively, which was prepared for suspending LSM powders at a constant temperature of 98 • C, and the solid content was controlled at 60 wt% for well-dispersion and moderate-viscosity. PAA and PEG were used as a dispersant and plasticizer with the mass ratio of 2% and 1.5% to LSM powders, respectively, for improving dispersibility and plasticity. The as-prepared LSM slurry was filled into glass tubes and then cooled down to room temperature to form gel bodies. After removing the LSM gel from the glass tube, the gel bodies were dried at 50 • C for 2 days, and then the obtained dehydrated bodies were pyrolyzed and sintered in the furnace (HTF 1800, Carbolite, Sheffield, UK) with a temperature rising rate of 1 • C per min. In a typical pyrolysis process, the dehydrated bodies were treated at 200 • C for 2 h to remove water, and then treated at 550 • C for 2 h to decompose organics. In the sintering treatment, the LSM bodies were sintered for 6 h at 800, 900, 1000, 1100, 1200 • C respectively. X-ray diffraction spectra (XRD) was carried out with an X-ray diffractometer (Bruker AXS, D8 Advanced, Billerica, MA, USA) using Cu Kα radiation (λ = 1.5418 Å) generated at 40 kV and 40 mA over a 2θ range of 20 • to 90 • with a sampling width of 0.02 • and a sampling speed of 10 • per min. The scanning electron microscopy (SEM) images of LSM ceramics at different sintering temperatures were collected by LEO 1530VP, ZEISS (Oberkochen, Germany), and the high-resolution transmission electron microscopy (HR-TEM) images and selected area electron diffraction (SAED) results were obtained by Tecnai G2 F20 S-TWIN, FEI (Hillsboro, OR, USA). The thermogravimetric analysis of the dehydrated body was tested by TG, TG209F3, NETZSCH (Selb, Germany), with the heating rate of 10 • C per min from room temperature to 900 • C. Both of the volume shrinkage and relative density were measured by a fast draining method. Compressive strength data were obtained using Zwick Roell materials testing machine (Z250, Zwick, Ulm, Germany), with the compression speed of 2 mm/min. The pore size distribution and porosity were investigated by mercury injection apparatus (AutoPore IV 9500 V1.09, Micromeritics Instrument Corp., Norcross, GA, USA), with a pressure range from 0.1 to 60,000 psia. The specific surface area was measured by the BET method (BET, Quantachrome Instruments, Boynton Beach, FL, USA), with an analysis gas of N 2 and bath temperature of 77.3 K.

Fabrication of LSM Sintered Bodies
LSM ceramic bodies were fabricated via gel casting and solid state sintering, as shown in Figure 1a. In detail, LSM slurry was prepared by suspending La 0.65 Sr 0.35 MnO 3 nanopowders in agar solutions at 98 • C, with the use of polyacrylic acid (PAA) and polyethylene glycol (PEG) as a dispersant and plasticizer, respectively. Then, we cast the as-prepared LSM slurry into molds (e.g., glass tubes) for gelation with a treatment of cooling below 4 • C. After removing the LSM gel from the mold, the as-fabricated cylindrical gel bodies dehydrated at 50 • C and subsequently sintered under high temperatures to form porous LSM ceramic bodies. Figure 1b shows the typical shapes of LSM gel, dehydrated and sintered body, respectively. Here, we observed that the cylindrical shape of LSM gel body was well-retained after both dehydration and high-temperature sintering treatment. Furthermore, neither the dehydrated nor sintered bodies have a fracture or crack, even though the diameter of LSM gel body decreases from~3.5 to~2.5 cm after dehydration and further to~1.8 cm after sintering treatment at 1200 • C. This firmly indicates that agar gel casting is suitable for fabricating LSM ceramic bodies.

Fabrication of LSM Sintered Bodies
LSM ceramic bodies were fabricated via gel casting and solid state sintering, as shown in Figure  1a. In detail, LSM slurry was prepared by suspending La0.65Sr0.35MnO3 nanopowders in agar solutions at 98 °C, with the use of polyacrylic acid (PAA) and polyethylene glycol (PEG) as a dispersant and plasticizer, respectively. Then, we cast the as-prepared LSM slurry into molds (e.g., glass tubes) for gelation with a treatment of cooling below 4 °C. After removing the LSM gel from the mold, the asfabricated cylindrical gel bodies dehydrated at 50 °C and subsequently sintered under high temperatures to form porous LSM ceramic bodies. Figure 1b shows the typical shapes of LSM gel, dehydrated and sintered body, respectively. Here, we observed that the cylindrical shape of LSM gel body was well-retained after both dehydration and high-temperature sintering treatment. Furthermore, neither the dehydrated nor sintered bodies have a fracture or crack, even though the diameter of LSM gel body decreases from ~3.5 to ~2.5 cm after dehydration and further to ~1.8 cm after sintering treatment at 1200 °C. This firmly indicates that agar gel casting is suitable for fabricating LSM ceramic bodies. In order to explore the ability of manufacturing in the secondary process, we cut the cylindrical LSM gel body into two parts and drilled hole-arrays with different diameters on LSM gel bodies, respectively. Similar to the pristine cylindrical LSM bodies, the shapes of both cut and drilled LSM bodies in Figure 1c,d have been well-retained after dehydration and high-temperature sintering treatment in spite of the significant volume shrinkage. Scanning electron microscopy (SEM) images clearly demonstrate the sharp straight edge in Figure 1e and hole-arrays in Figure 1f of the cut and drilled LSM bodies after the sintering treatment at 1200 °C, respectively. Importantly, no fracture or crack occurs on the surface of sintered bodies or at the cut edge and hole edge, even inside the holes. In order to explore the ability of manufacturing in the secondary process, we cut the cylindrical LSM gel body into two parts and drilled hole-arrays with different diameters on LSM gel bodies, respectively. Similar to the pristine cylindrical LSM bodies, the shapes of both cut and drilled LSM bodies in Figure 1c,d have been well-retained after dehydration and high-temperature sintering treatment in spite of the significant volume shrinkage. Scanning electron microscopy (SEM) images clearly demonstrate the sharp straight edge in Figure 1e and hole-arrays in Figure 1f of the cut and drilled LSM bodies after the sintering treatment at 1200 • C, respectively. Importantly, no fracture or crack occurs on the surface of sintered bodies or at the cut edge and hole edge, even inside the holes. This strongly implies the remarkable capability of agar-based LSM gel bodies for manufacturing in the secondary process. Of note, the hole-diameter ranges from 340 to 500 µm, appropriate for fabricating cathode-supported SOFCs in sub-millimeter scale.
Moreover, thermogravimetric analysis (TGA) of the dehydrated body was conducted to investigate the removal of agar during the heating stage. The TGA curve in a range from room temperature (RT,~25 • C) to 900 • C depicts that the degradation of the dehydrated body can be roughly divided into three weight-loss stages of RT~280 • C, 280~460 • C and 460~820 • C, respectively, as shown in Figure S1 (Supplementary Materials). In the first stage, the weight of the gel body decreases~2.7% as the temperature rises to 280 • C, corresponding to water evaporation. Furthermore, we observed a weight loss of~3.4% in the second stage at 280~460 • C and a weight loss of~3.5% in the third stage at 460~820 • C, which should be attributed to the pyrolysis of organic materials including PEG, PAA and agar. Importantly, the weight remains nearly invariable when the temperature is higher than 800 • C, strongly indicating that all the organic materials have been completely decomposed before the high-temperature sintering treatment of LSM powders.

Microstructures of LSM Sintered Bodies
Next, we studied LSM sintered bodies via X-ray diffraction (XRD). This strongly implies the remarkable capability of agar-based LSM gel bodies for manufacturing in the secondary process. Of note, the hole-diameter ranges from 340 to 500 μm, appropriate for fabricating cathode-supported SOFCs in sub-millimeter scale. Moreover, thermogravimetric analysis (TGA) of the dehydrated body was conducted to investigate the removal of agar during the heating stage. The TGA curve in a range from room temperature (RT, ~25 °C) to 900 °C depicts that the degradation of the dehydrated body can be roughly divided into three weight-loss stages of RT~280 °C, 280~460 °C and 460~820 °C, respectively, as shown in Figure S1 (Supplementary Materials). In the first stage, the weight of the gel body decreases ~2.7% as the temperature rises to 280 °C, corresponding to water evaporation. Furthermore, we observed a weight loss of ~3.4% in the second stage at 280~460 °C and a weight loss of ~3.5% in the third stage at 460~820 °C, which should be attributed to the pyrolysis of organic materials including PEG, PAA and agar. Importantly, the weight remains nearly invariable when the temperature is higher than 800 °C, strongly indicating that all the organic materials have been completely decomposed before the high-temperature sintering treatment of LSM powders.

Microstructures of LSM Sintered Bodies
Next, we studied LSM sintered bodies via X-ray diffraction (XRD).  We further characterized the microstructure of LSM sintered bodies via SEM investigation. As High-resolution transmission electron microscopy (HR-TEM) with selected area electron diffraction (SAED) was used to further analyze the crystal structure of the LSM sintered bodies. The lattice planes with a distance of~2.72 Å can be observed in the HR-TEM images of pristine LSM powders in Figure 2b and LSM sintered bodies at different sintering temperatures in Figure 2c-g inset, which is in good agreement with the (104) plane of the perovskite La 0.65 Sr 0.35 MnO 3 structure. Moreover, the SAED patterns in Figure 2c-g inset, measured from [1] zone-axis demonstrate that the lattice parameters are a = 5.4 Å, b = 5.4 Å and c = 15.3 Å, which are consistent with data in other reports.
We further characterized the microstructure of LSM sintered bodies via SEM investigation. As shown in Figure 3, the sintering temperature significantly influences the microstructure of the LSM sintered body. The SEM image of the LSM dehydrated body in Figure 3a demonstrates that the raw LSM nanopowders with an average size of~210 nm have been tightly fixed by the binder of agar (4% agar concentration). When sintering at 800 • C, the binder of agar was completely removed and consequently LSM powders congregated with a slight size growth from~210 to~225 nm, as shown in Figure 3b. When sintering at 900 • C, LSM powders began coalescing and the average size grew up tõ 260 nm in Figure 3c. As the sintering temperature increased to 1000 • C, LSM powders coalesced to form porous structures with the average size exceeding 320 nm, as in Figure 3d. Figure 3e shows the microstructure of the LSM sintered body with the sintering temperature of 1100 • C. Obviously, the LSM powders tremendously grew into large blocks and their crystallinity significantly enhanced, whereas the porous structure disappeared in contrast with the LSM sintered body with the sintering temperature of 1000 • C. When the sintering temperature ascended to 1200 • C, LSM powders were sintered into a solid LSM ceramic monolith, as illustrated in Figure 3f. This indicates that high-temperature sintering treatment facilitates the densification of LSM ceramics.  Figure 3a demonstrates that the raw LSM nanopowders with an average size of ~210 nm have been tightly fixed by the binder of agar (4% agar concentration). When sintering at 800 °C, the binder of agar was completely removed and consequently LSM powders congregated with a slight size growth from ~210 to ~225 nm, as shown in Figure 3b. When sintering at 900 °C, LSM powders began coalescing and the average size grew up to ~260 nm in Figure 3c. As the sintering temperature increased to 1000 °C, LSM powders coalesced to form porous structures with the average size exceeding 320 nm, as in Figure 3d. Figure 3e shows the microstructure of the LSM sintered body with the sintering temperature of 1100 °C. Obviously, the LSM powders tremendously grew into large blocks and their crystallinity significantly enhanced, whereas the porous structure disappeared in contrast with the LSM sintered body with the sintering temperature of 1000 °C. When the sintering temperature ascended to 1200 °C, LSM powders were sintered into a solid LSM ceramic monolith, as illustrated in Figure 3f. This indicates that hightemperature sintering treatment facilitates the densification of LSM ceramics.

Properties of LSM Sintered Bodies
During the process of dehydration and high-temperature sintering treatment, we observed that the significant linear and volume shrinkage were closely related to the fabrication conditions, e.g., the agar content and the sintering temperature. Figure 4a shows the effects of the agar content during dehydration. When the agar content increased from 1% to 4%, the linear and volume shrinkage remained around 18% and 46%, respectively. However, the linear and volume shrinkage increased to ~29% and ~64%, respectively, when the agar content was 5%. This indicates that a small amount of agar content can make a great difference in the linear and volume shrinkage during dehydration. Moreover, the LSM green bodies with the 4% agar concentration were utilized to investigate the shrinkage during high-temperature sintering treatment. Figure 4b shows the effects of temperature during sintering treatment. As the sintering temperature rose from 800 °C to 1200 °C, the linear shrinkage gradually increased from ~27% to ~48% and the volume shrinkage gradually increased from ~62% to ~79%. This shows that high temperatures promote the linear and volume shrinkage during sintering treatment.

Properties of LSM Sintered Bodies
During the process of dehydration and high-temperature sintering treatment, we observed that the significant linear and volume shrinkage were closely related to the fabrication conditions, e.g., the agar content and the sintering temperature. Figure 4a shows the effects of the agar content during dehydration. When the agar content increased from 1% to 4%, the linear and volume shrinkage remained around 18% and 46%, respectively. However, the linear and volume shrinkage increased tõ 29% and~64%, respectively, when the agar content was 5%. This indicates that a small amount of agar content can make a great difference in the linear and volume shrinkage during dehydration. Moreover, the LSM green bodies with the 4% agar concentration were utilized to investigate the shrinkage during high-temperature sintering treatment. Figure 4b shows the effects of temperature during sintering treatment. As the sintering temperature rose from 800 • C to 1200 • C, the linear shrinkage gradually increased from~27% to~48% and the volume shrinkage gradually increased from~62% to~79%. This shows that high temperatures promote the linear and volume shrinkage during sintering treatment. Furthermore, we measured the porosity, specific surface area and relative density of LSM sintered bodies at different sintering temperatures. First, the pore size distribution of LSM sintered bodies, as shown in Figure S2 (Supplementary Materials) were measured via mercury injection apparatus and the detailed average pore diameter were listed in Table S1 (Supplementary Materials). The average pore diameter gradually increased from 200.6 nm to 305.5 nm when the sintering temperature increased from 800 °C to 1000 °C, and dramatically increased to 604.4 nm and 1.72 μm when the sintering temperature was 1100 °C and 1200 °C, respectively. However, we note that the pore volume gradually decreased from ~0.6 mL/g to ~0.4 mL/g when the pore diameter was less than 500 nm, and then dramatically decreased to ~0.05 mL/g and ~0.004 mL/g when the sintering temperature was 1100 °C and 1200 °C, respectively. This strongly indicates that increasing temperatures benefit LSM nanopowders sintering. Obviously, the ultrasmall pore volume with the pore diameter less than 500 nm indicates the dense sintered LSM bodies, which is consistent with the SEM image of LSM body with the sintering temperature at 1200 °C. On the other hand, the pore size larger than 500 nm should be attributed to air holes and cracks which origin from the process of gel casting and high temperature sintering, respectively. Then, we calculated the porosity of LSM sintered bodies at different sintering temperatures. As shown in Figure 4c, the porosity of LSM sintered bodies is ~69% when the sintering temperature is 800 °C, and then it decreases to ~62% and ~60% when increasing the temperature to 900 °C and 1000 °C, respectively. Furthermore, the porosity dramatically decreased to ~34% and ~28% when the sintering temperature increased to 1100 °C and 1200 °C, respectively. This trend is consistent with the pore volume results. Moreover, we investigated the specific surface area of LSM sintered bodies via the BET method. In Figure 4c, the specific surface area decreased from 7.7 m 2 ·g −1 to 0.000014 m 2 ·g −1 when the sintering temperature increased from 800 °C to 1200 °C. Such declining trend is consistent with the result of porosity and the SEM investigation in Figure 3. Additionally, we measured the relative density of LSM sintered Furthermore, we measured the porosity, specific surface area and relative density of LSM sintered bodies at different sintering temperatures. First, the pore size distribution of LSM sintered bodies, as shown in Figure S2 (Supplementary Materials) were measured via mercury injection apparatus and the detailed average pore diameter were listed in Table S1 (Supplementary Materials). The average pore diameter gradually increased from 200.6 nm to 305.5 nm when the sintering temperature increased from 800 • C to 1000 • C, and dramatically increased to 604.4 nm and 1.72 µm when the sintering temperature was 1100 • C and 1200 • C, respectively. However, we note that the pore volume gradually decreased from~0.6 mL/g to~0.4 mL/g when the pore diameter was less than 500 nm, and then dramatically decreased to~0.05 mL/g and~0.004 mL/g when the sintering temperature was 1100 • C and 1200 • C, respectively. This strongly indicates that increasing temperatures benefit LSM nanopowders sintering. Obviously, the ultrasmall pore volume with the pore diameter less than 500 nm indicates the dense sintered LSM bodies, which is consistent with the SEM image of LSM body with the sintering temperature at 1200 • C. On the other hand, the pore size larger than 500 nm should be attributed to air holes and cracks which origin from the process of gel casting and high temperature sintering, respectively. Then, we calculated the porosity of LSM sintered bodies at different sintering temperatures. As shown in Figure 4c, the porosity of LSM sintered bodies is~69% when the sintering temperature is 800 • C, and then it decreases to~62% and~60% when increasing the temperature to 900 • C and 1000 • C, respectively. Furthermore, the porosity dramatically decreased to~34% and 28% when the sintering temperature increased to 1100 • C and 1200 • C, respectively. This trend is consistent with the pore volume results. Moreover, we investigated the specific surface area of LSM sintered bodies via the BET method. In Figure 4c, the specific surface area decreased from 7.7 m 2 ·g −1 to 0.000014 m 2 ·g −1 when the sintering temperature increased from 800 • C to 1200 • C. Such declining trend is consistent with the result of porosity and the SEM investigation in Figure 3. Additionally, we measured the relative density of LSM sintered bodies at different sintering temperatures. Figure 4c demonstrates that the relative density gradually increased from~50% to~69% with the sintering temperature rising from 800 • C to 1200 • C, in accordance with the increase of linear and volume shrinkage in Figure 4b. We further tested the compressive strength of LSM sintered bodies at different sintering temperatures. As the sintering temperature rose from 800 • C to 1000 • C, the compressive strength of LSM sintered bodies increased exponentially from 2 MPa to 5.6 MPa. Then, the value rose sharply to 15 MPa at 1100 • C, and it increased to 25 MPa at 1200 • C. This trend may result from their increasingly solid structures [26].

Discussion
In a traditional acrylamide gel casting process, an irreversible free radical triggered polymerization was used to form gel bodies, which significantly depended on many reaction conditions such as concentration, temperature, pH values, etc. In comparison, a reversible agar gelation was utilized to form gel bodies during a typical agar gel casting process, which can be simply controlled by temperature tuning. When the temperature is lower than glass state temperature, agar aqueous solutions were solidified to agar gels, conversely, agar gels were melted to solutions when the temperature is higher than glass state temperature. This indicates that controlling the process of agar gelation is easier than that of acrylamide polymerization. Furthermore, APS is a sensitive radical generator that was used for acrylamide polymerization in the gel casting process. However, it could be decomposed by many transition metal oxides and thus limited the use of acrylamide polymerization for gel casting transition metal oxides. In contrast, agar is completely inert to transition metal oxides under mild conditions, which might be more suitable for gel casting transition metal contained ceramics. Moreover, acrylamide polymerization is an irreversible chemical reaction, whereas agar gelation is a reversible process that facilitates remolding gel bodies in the recycling process. In addition, agar-based gel bodies are able to manufacture in the secondary process, including cutting and drilling in meso-scale, which exhibits great potential for the fabrication of cathode-supported micro-SOFC.
High-temperature sintering treatment is another important process that directly determines the linear and volume shrinkage, specific surface area, porosity, relative density, and compressive strength of LSM ceramics. As the rise of sintering temperature, the specific surface area and porosity were descending, whereas the relative density and compressive strength were ascending. Coupling with the SEM images of LSM ceramics sintering at different temperatures, we propose a probable sintering mechanism to understand the high-temperature sintering treatment in Figure S3 (Supplementary Materials). At the initial stage of dehydrated body, LSM nanoparticles were tightly fixed in the agar gel skeleton at room temperature. When sintering at 800 • C, the agar skeleton was completely decomposed and the rest of LSM nanoparticles conglomerated and remained the shape of dehydrated body. Such LSM nanoparticles started to agglomeration when the sintering temperature reached 900 • C. A distinctive porous structure emerged with inter-connected pores and obvious agglomeration when the sintering temperature further increased to 1000 • C. When sintering at 1100 • C, the size of LSM particles dramatically increased and the crystallinity significantly enhanced as well. On the other hand, the porosity declined significantly, especially the pore size distribution in range from 200 to 500 nm. When the sintering temperature rose to 1200 • C, the porosity decreased continuously and the pores with the size distribution in range of 200~500 nm were eliminated, resulting in the steadily enhanced compressive strength which was able to meet the requirement of the Micro-SOFC electrode [27].

Conclusions
In summary, we have developed a low-cost and environmentally friendly LSM ceramics method for fabricating LSM ceramics with certain shapes via using agar gel casting and high temperature sintering. During the agar gel casting process, a physical method of temperature tuning was used to form gel bodies, rather than a chemical method of radical-triggered polymerization in a traditional acrylamide gel casting process. Based on such reversible temperature-tuning physical process, the as-fabricated LSM gel bodies facilitate not only manufacturing in the secondary process but also remolding and recycling during the gel casting process. During high-temperature sintering process, the relationships between the sintering temperature, microstructure, and the properties including the specific surface area, relative density, porosity, and compressive strength were discussed. Our studies are of potential meaning for the design and construction of high-temperature energy conversion and storage devices.
Supplementary Materials: The following are available online at http://www.mdpi.com/1996-1944/12/6/848/s1, Figure S1: The TG curve of the LSM dehydrated body; Figure S2: Pores size distribution of LSM sintered bodies with different sintering temperatures; Figure S3: A diagram of LSM sintered bodies with different sintering temperatures; Table S1: The average pore diameter of sintered at different temperature.
Funding: This research received no external funding.