With the advancement of the Materials Genome Initiative and the establishment and improvement of the glass database, data-driven machine-learning methods penetrate the field of glass materials, and remarkable progress is made in the modeling of the physical, mechanical, and optical properties of glass materials. In recent years, oxide glasses have found increasingly widespread applications in the field of electronic applications, and their electrical properties as critical indicators have attracted much attention. However, modeling on the electrical properties of oxide glasses remains a challenge, and insufficient data suppress the model's performance. To address the issue of limited data availability on the electrical properties of oxide glasses, this work was to propose a data augmentation framework named WGAN-GP-CP tailored for glass materials.

Based on the Wasserstein generative adversarial network with gradient penalty (WGAN-GP) model, an additional composition penalty term (CP) was added to the generator's loss function, and a method for evaluating sample quality was proposed, which could assess the quality of the generated samples from three aspects, i.e., diversity, accuracy, and uniqueness. Moreover, the XGBoost algorithm was employed for model training, and the model was interpreted through SHAP single-feature analysis and feature interaction analysis.

The trained generators can generate high-quality synthetic samples, expanding the existing datasets effectively. The results of comparative studies demonstrate that the data-augmented models exhibit mitigated overfitting and significantly enhanced generalization capability. The generalization performances of the room-temperature bulk resistivity, relative dielectric constant, and dielectric loss models increase from 0.784 to 0.838, 0.862 to 0.897, and 0.801 to 0.861, respectively. The results obtained from SHAP analysis are generally consistent with the classical physicochemical understanding of the electrical properties of oxide glasses. In addition, some interesting mixing effects and interactive relationships are also revealed.

The data augmentation framework proposed in this work offered a strategy for developing high-performance data-driven models under data scarcity conditions. The insights from SHAP single-feature analysis and feature interaction analysis could provide an important guidance for a deeper understanding of the relationship between the composition and electrical properties of oxide glasses. This research shifted the optimization of oxide glass electrical properties from empirically driven trial-and-error methods to data-driven scientific design frameworks, laying a foundation for the development of high-performance glass materials in the field of electronic applications.

Solid oxide fuel cell (SOFC) stacks depend on metallic interconnects to ensure the performance with cathode-side protection and interfacial resistance as key determinants. The existing coatings like perovskite, active element oxides and spinel all have drawbacks. For instance, perovskite coatings fail to inhibit oxygen ion diffusion, while active element oxides are typically thin and porous. In contrast, spinel coatings have a promise due to their lower densification temperature and ability to suppress chromium volatility. However, there is little work on the contact resistance. In this work, a Mn-Co spinel coating was applied to SUS441 stainless steel to reduce both oxidation and interfacial resistance. This approach could offer a viable solution for optimizing the performance of SOFC stacks.

SUS441 was chosen as an interconnect substrate material, and all the samples were cut to small pieces with the dimensions of 10.0 mm × 10.0 mm × 1.5 mm. Manganese nitrate and cobalt nitrate (AR, Sinopharm Group Co., Ltd., China) were dispersed in ethanol solvent, with dispersant, binder, and defoamer added to prepare a precursor solution. A wet-spray device was used to deposit Mn_1.5Co_1.5O₄ coating on the SUS441 substrate (coated SUS441), which was then dried in air and calcined at 850 ℃ for 10 h.

The area-specific resistance (ASR) of the samples was measured by a four-terminal method with a CHI760e electrochemical workstation (Shanghai Chenhua Instrument Co., Ltd., China), with a voltage range of -1 to 1 V. The interfacial contact resistance was calculated based on the ASR values.

The thermal expansion behavior was characterized by a model DIL402C dilatometer (Netzsch Co., Germany) at a heating rate of 5 ℃/min. The microstructures were determined by a model S4800 scanning electron microscope (Hitachi Co., Japan). The oxidation mass gain was monitored by a model FA2104 electronic balance (Shanghai Shunyu Hengping Scientific Instruments Co., Ltd., China). A three-dimensional surface profile was obtained by a model LSM700 laser confocal microscope (Zeiss Co., Germany).

The coated SUS441 exhibits an uneven surface but a dense cross-section free of cracks or bubbles, indicating a robust adhesion between the coating and substrate. The Mn-Co spinel coating substantially reduces the interconnect's resistance of 0.47 mΩ·cm², compared to 3.29 mΩ·cm² for uncoated SUS441. Also, the coating enhances the activation energy (E_a) for electrical conductivity from 0.59 eV to 0.91 eV, thereby slowing electron migration and reducing the oxidation rate.

The results of long-term testing at 750 ℃ show that the ASR of uncoated SUS441 increases from 26.07 mΩ·cm² to 52.41 mΩ·cm² after 720 h, then gradually decreases and stabilizes at 25.54 mΩ·cm². This may result from the maturation and reconstruction of the oxide layer, which lowers the resistance. In contrast, the coated SUS441 has an initial ASR of 3.96 mΩ·cm², which increases to 16.38 mΩ·cm² after 300 h and then slowly declines to 11.97 mΩ·cm² at 820 h. These findings demonstrate that the Mn-Co coating significantly enhances the high-temperature oxidation resistance of SUS441.

The oxidation mass gain is a key indicator of interconnect oxidation resistance. The coated and uncoated SUS441 interconnects both exhibit a rapid mass gain in the first 200 h. After 200 h, the mass gain rate of the coated SUS441 slows and stabilizes, whereas the uncoated SUS441 further increases. The dense Mn-Co coating effectively blocks oxygen penetration and metal ion migration, thereby slowing oxidation and enhancing resistance. The relationship between the square of oxidation mass gain and time indicates a change in oxidation behavior after approximately 200 h, likely due to the thickening of the oxide layer hindering further oxidation. As the oxide layer thickens, the internal mass transfer becomes more difficult, slowing the oxidation rate. The K_p value decreases by one order of magnitude during the slow oxidation phase, compared to the initial rapid stage.

The coating has a limited impact on the thermal expansion of the interconnect but brings the expansion coefficient of SUS441 closer to that of the La_0.6Sr_0.4Co_0.2Fe_0.8O₃ (LSCF) cathode, thus improving the thermal compatibility. The initial interfacial contact resistance between SUS441 and LSCF is 3.54 mΩ·cm², stabilizing at 14.57 mΩ·cm². For coated SUS441 and LSCF, the initial interfacial contact resistance decreases from 20.78 mΩ·cm² to 7.99 mΩ·cm². The Mn-Co coating likely improves the interface microstructure, reducing defects and roughness, and enhancing electron transfer. The analysis of laser confocal microscopy indicates that the roughness matching value between SUS441 and LSCF is 0.605, and it is 1.156 for coated SUS441, indicating better surface compatibility and contact with LSCF.

The Mn-Co spinel coating was coated on the surface of SUS441 interconnect, and its effect on suppressing the interconnect's oxidation behavior and reducing interfacial resistance were investigated. The results showed that the coating significantly reduced the ASR of SUS441 from 3.29 mΩ·cm² to 0.47 mΩ·cm² at 800 ℃, maintaining a relatively low ASR of 11.97 mΩ·cm² after 800 h oxidation. The results of oxidation mass gain tests indicated that the coating effectively reduced the oxidation rate of coated SUS441, which was only 43% of that of the uncoated sample. For the interfacial properties, the contact resistance between the Mn-Co coated SUS441 and the LSCF cathode was 7.99 mΩ·cm², which was just 55% of that of the uncoated sample, with improved interfacial roughness matching. These findings could demonstrate that the Mn-Co spinel coating effectively mitigated the oxidation rate and interfacial resistance of SUS441, thereby enhancing its high-temperature oxidation resistance.

The advancements in glass property calculations are shifting from data accumulation to high-efficiency prediction, with databases differing in scale, openness, algorithm integration, and applicability. Future developments will focus on data sharing, multi-method integration, and experimental-computational-machine learning synergies, providing an enhanced technical support for both scientific research and industrial applications of glass materials. Some methodologies can merge advances in materials science with cutting-edge computational tools. High-throughput preparation techniques promise a rapid discovery of new glass compositions via enabling swift synthesis and testing. Pairing these with advanced characterization methods like spectroscopy or diffraction can generate datasets for AI models, driving a further innovation.

Electrochromic device (ECD) is comprised of five superimposed layers, i.e., transparent conducting layer, electrochromic layer, ion conductor layer, ion storage layer and another transparent conducting layer, respectively. It can modulate the amount of solar radiation transmitting through it under applied voltage, often used as smart windows or facades to adjust the light and heat entering buildings proactively, which can sufficiently reduce the energy consumption. The existing ECDs are mainly fabricated by a magnetron sputtering method, which has a low productivity and high cost, especially for the ion conductor layer. Sol-gel method is a simple and relatively cheap method for preparing thin films, and massive researches are conducted on sol-gel electrochromic thin films such as tungsten oxide, nickel oxide etc.. In this work, an ion conductor layer was prepared by a sol-gel method, and its application in electrochromic device and their performance were also investigated.

Lithium tantalite sol was synthesized with lithium acetate (LiAc) and tantalum pentaethoxide (TaEt) as precursors and 1,2-Propanediol as a solvent. The molar ratio of LiAc and TaEt was 1∶1. Lithium tantalite thin films were prepared by a spin coating method and heat-treated in air at 400 ℃ for 2 h. Some of the sol was dried and the subsequently formed powder was heated at 600-700 ℃. The phase compositions of the films and powders were characterized by X-ray diffraction (XRD), and the electrochemical properties of thin films were analyzed.

The electrochromic devices with a structure of ITO/NiO/LiTaO₃/WO₃/ITO were prepared by PVD method and subsequent sol-gel method. The tungsten oxide or nickel oxide thin film layer was firstly sputtered on the ITO glass and then lithium tantalite thin films were spin-coated onto the as prepared films. After heating process at 400 ℃ for 2 h, another layer of the tungsten oxide or nickel oxide films were sputtered, and another layer of ITO thin film was finally sputtered as a conducting electrode. The electrochromic devices were noted as EC-N when lithium tantalite was spin-coated onto nickel oxide films and as EC-W when lithium tantalite was spin-coated onto tungsten oxide films. The transmittance changes were measured by UV-vis-IR spectrometer.

The XRD patterns show that powders dried and heated from the sol are a polycrystalline lithium tantalite, and thin films are amorphous. The analysis of electrochemical impedance spectroscopy indicates that the sol-gel lithium tantalite thin film has an ionic conductivity of 7.44×10^-7 S/cm at room temperature, which is comparable to that of sputtered film. As for the devices, the XRD patterns show that nickel oxide thin film layers are both polycrystalline in EC-N and EC-W, while tungsten oxides is polycrystalline in EC-W and amorphous in EC-N. The XRD patterns and XPS spectra also show the existence of WO_3-x phase in polycrystalline tungsten oxide films.

For electrochromic properties of the two groups of devices, transmittance regulations are measured at a fixed wavelength of 550 nm. For both groups, the differences of transmittance between colored and bleached state increase with increasing voltage. The maximum of transmittance change for EC-N is 26% at 5 V, with transmittance of around 72% at bleached state and 46% at colored state. Its coloring time is 50 s and bleaching time is 56 s. The results of cyclic test show that the differences of colored and bleached states keep stable, no obvious degeneration occurs after 60 cycles. The transmittance changes for EC-W have a lower value when applied the same voltages as in EC-N, and the switching speed is much slower. Its transmittance change is 14% at 3 V, while the coloring and bleaching time are both larger than 2 min, exceeding the setting range. It can be concluded that EC-N has a better property for regulation of visible light, and crystallinity can slow the switching process.

The transmittance spectra of colored states in vis-NIR range show that EC-W has a significant modulating performance for NIR, which can be attributed to the existence of WO_3-x components. As reported, oxygen deficient components can generate a local surface plasmon resonance effect that can result in absorption in the spectral range of NIR.

Electrochromic devices fabricated by a process that lithium tantalite was spin-coated on nickel oxide had better electrochromic properties in a visible spectral range, with larger optical modulations and a higher switching speed less than 1 min. The devices with lithium tantalite spin-coated on the tungsten oxide films could have a slower coloring and bleaching rate, while showing a better near-infrared modulation effect. These results indicated a routine for the realization of electrochromic devices that could modulate light and heat simultaneously and independently.

Compared to Co-based cathode materials, Fe-based perovskite materials exhibit superior thermal stability and electrochemical stability, but they have lower conductivity and redox activity. The Fe-based perovskite materials are regarded as one of the cathode materials with a great development potential for SOFCs due to their lower thermal expansion coefficient and cost. In the LnBaFe₂O_5+δ (Ln = lanthanide elements, Y) double perovskite materials, PrBaFe₂O_5+δ (PBF) has the lowest activation energy for the redox reaction, making it a promising alternative material for SOFC cathodes. For the PBF materials, there are a few reports on their crystal structure and redox reaction mechanisms. There is still a debate regarding the tetragonal and cubic structures of PBF materials. Also, the mechanism of the redox reaction remains unclear and requires a further in-depth investigation. This study was to prepare the PBF cathode materials by a sol-gel method. In addition, the synthesis process, crystal structure, and redox reaction mechanisms of PBF materials were also investigated.

The average binding energy of the possible structures of PBF was calculated by the Cambridge Sequential Total Energy Package (CASTEP) module in Material Studio software. The reflex module in Materials Studio was used to simulate the X-ray diffraction (XRD) patterns after optimizing the structures. The PBF powder was prepared by a sol-gel method, and the precursors were analyzed by thermgravity-differential thermal analysis (TG-DTA), X-ray diffraction (XRD) and transmission electron microscopy(TEM). The calcined samples were treated in air, 20% (in volume) H₂(H₂+N₂) atmosphere, and pure H₂ at 800 ℃ for 20 h. In addition, the electrochemical impedance spectra of the PBF|SDC|PBF symmetrical cell were measured, and analyzed via distribution of relaxation times (DRT).

The simulated XRD patterns show distinct differences in the XRD peaks of the four PBF structures with the main difference between the tetragonal and simple cubic structures after 80°. The characteristic double peak of the double perovskite is attributed to an increased lattice distortion caused by an increase in oxygen vacancy defects, while its structural symmetry remains unchanged. The tetragonal structure has the lowest average binding energy, while the simple cubic structure has the highest. This indicates that the likelihood of PBF adopting a simple cubic structure is minimal, whereas the likelihood of it adopting a tetragonal structure is maximal.

The results of TG-DTA and XRD indicate that the precursors form BaFeO₃ and PrFeO₃ heat-treated at 800 ℃ and a subsequent two-phase solid solution process after 800 ℃. Pure PBF is obtained after roasting in air at 1200 ℃ for 5 h. In a 20%H₂(H₂+N₂) atmosphere, pure PBF can be achieved at 800 ℃, indicating that the 20%H₂(H₂+N₂) treatment accelerates the solid solution of BaFeO₃ and PrFeO₃. The PBF is structurally stable in both air and a 20%H₂(H₂+N₂) atmosphere, but decomposes into Fe, BaFeO₃, and Pr₂O₃ in pure H₂, indicating that PBF material decomposes under pure hydrogen and is not suitable for use on the anode side. Also, the occupancy of O in the [Pr-O] layer decreases, indicating that more oxygen vacancies are generated after reduction. The analysis of the crystal structure shows that the unit cell is elongated in a 20%H₂(H₂+N₂) atmosphere due to the formation of more oxygen vacancies in the [Pr-O] layer.

Based on the different relaxation times of various cathodic reactions, the DRT analysis indicates that the limiting step of the ORR at 400−550 ℃ involves the ionization of oxygen atoms and the transport of oxygen ions, while that at 600−700 ℃ involves the chemisorption of oxygen and the dissociation of oxygen molecules. At 700−800 ℃, the limiting step is related to the physisorption of oxygen. Clearly, the conclusions drawn from time-domain analysis differ from those obtained through conventional impedance spectroscopy. At 750−800 ℃, time-domain analysis indicates that the limiting step affecting the ORR is the physisorption of oxygen, whereas conventional impedance spectroscopy indicates that it is the ionization of oxygen atoms and the transport of oxygen ions. This study posits that both sets of results can serve as a basis for optimizing the oxygen catalytic performance of PBF materials.

This study investigated the formation process, structure, stability, and oxygen catalytic performance of PBF materials by DFT calculations, XRD, TEM, EIS, and DRT analysis. The PBF synthesized through the solid solution formation of PrFeO₃ and BaFeO₃ at 800 ℃ exhibited a tetragonal structure (i.e., space group: P4/mmm). The crystal structure remained stable in air and 20%H₂(H₂+N₂) atmosphere, but partially decomposed into Fe, BaFeO₃, and Pr₂O₃ in pure hydrogen. The limiting steps of the oxygen reduction reaction (ORR) were identified as the ionization of oxygen atoms and the transport of oxygen ions at 400−550 ℃, chemisorption of oxygen and dissociation of oxygen molecules at 600−700 ℃, and physisorption of oxygen at 700−800 ℃.

With the rapid iteration of smart displays, especially smartphones, cover plate glass as one of the key materials has made recent progress, becoming an important component in the field of electronic information display applications. Aluminosilicate glass with its unique properties (i.e., good impact resistance, scratch resistance, and high hardness, as well as excellent chemical and thermal stability) is an ideal candidate material for plate cover glass. There is relatively in-depth research on the influence of composition changes in aluminosilicate glass on its structure and properties, but most of the existing research focuses on the short-range structure (<5 Å) of the aluminosilicate glass network structure, while there is less research on its medium-range structure (5-20 Å). In this work, the influence of multi-layer network structure of aluminosilicate glass on its properties was investigated by molecular dynamics simulation and experiments.

The relationship between the composition-structure-properties of glass was investigated by experimental methods and molecular dynamics simulations. The glass samples were prepared by a conventional high-temperature melting method. The raw materials were weighed and mixed uniformly according to the molar ratio of oxides, put into a platinum-rhodium crucible (90% Pt and 10% Rh), and then heated in a high-temperature lifting furnace at 1640 ℃ for 2 h. After melting, the crucible containing the molten glass was removed and poured onto a preheated copper mold. Once it solidified, it was transferred to an annealing furnace, followed by natural cooling to room temperature to eliminate internal stresses in the glass, resulting in uniform, transparent bulk glass. The glass was then cut and mechanically polished to obtain the samples with various sizes.

The glass samples were simulated, and the simulated structure was a cubic box composed of approximately 10000 atoms. The initial dimensions of the simulation box were calculated based on predicted density and atomic mass. The initial structure was optimized by a soft potential to ensure structural integrity and prevent atomic loss. The potential function used was the Buckingham potential, and the Ewald summation method was used to handle long-range Coulomb interactions. The cutoff radius was set to 10 Å, with an integration time step of 0.001 ps. The initial structure was randomly generated by an open-source software named ATOMSK.

The statistical results of the short-range structural characteristics of silicate glass indicate that there are no significant changes in the position and intensity of the O—O peak, and the intensity of the Al—O peak near 1.7 Å gradually increases as Al₂O₃ content increases. The number of Al—O structural units in the glass network structure increases, having a clear symmetrical distribution with aluminum primarily in a four-coordinate environment. The strength of the Si—O bond decreases with the reduction of SiO₂. The number of [SiO₄] tetrahedral groups decreases, and some alkaline earth metal ions in the glass network structure transform into ions that serve to compensate for the charge of the [AlO₄] tetrahedral groups.

The statistical analysis of the medium-range structural characteristics of aluminosilicate glass indicates that as Al₂O₃ content increases, the Q value of the first sharp diffraction peak (FSDP) shifts towards higher values, the ring size distribution shows a certain sharpening degree with the decreasing proportions of small rings (i.e., 3-membered and 4-membered rings) and large rings (i.e., ≥7-membered rings), while increasing the proportions of medium-sized rings (i.e., 5-membered and 6-membered rings). The smaller rings, such as the three-membered and four-membered rings, typically possess a higher energy and are more prone to structural rearrangement or breakage, whereas the larger rings, such as the five-membered and six-membered rings, are relatively stable. This indicates a reduction in the medium-range disorder of the glass network structure, resulting in a denser network structure.

The mechanical properties of the glass (i.e., density, elastic modulus, and Vickers hardness) gradually increase with the increase of Al₂O₃ content. The mechanical characteristics of the glass are positively correlated to the density of its network structure. The increase in the content of the [AlO₄] network structure makes the network structure denser, while the combined effect of [AlO₄] and [SiO₄] gradually enhances the integrity of the glass network. This results in a decrease in the average coefficient of thermal expansion, an increase in the strain point and softening point, and an increase in high-temperature viscosity.

The relationship between the composition-structure-properties of aluminosilicate glass was elucidated through experiments and molecular dynamics simulations. The substitution of Al³⁺ for Si⁴⁺ induced changes in the short-range and medium-range network structures of the glass, leading to an increase in the bridging oxygen content and a sharpening of the ring size distribution. The structural factor could shift towards higher values at the position of the first sharp diffraction peak (FSDP), resulting in an increase in the order of the short-range and medium-range network structures, and making the network structure denser. Consequently, the density, elastic modulus, Vickers hardness, strain point, softening point, and viscosity of the glass melt all increased, while the average coefficient of thermal expansion decreased.

Methane as a significant energy and chemical raw material boasts higher energy density, lower pollution, and abundant reserves, compared to coal or petroleum. The reforming of methane to syngas is one of the key technologies for its clean and efficient utilization. The produced syngas can be applied in hydrogen production, chemical synthesis, combustion, and as fuel gas for solid oxide fuel cells (SOFC). The chemical energy in the fuel gas can be directly converted into electrical energy when produced syngas used as SOFC fuel gas, serving as an important pathway for the clean and efficient utilization of carbon-based fuels. The dry reforming of methane (DRM) is a promising technology that converts methane and carbon dioxide into syngas (i.e., CO and H₂), offering notable environmental and economic benefits. However, the DRM reaction is confronted with some challenges like high CO₂ costs and propensity for carbon deposition. This paper was to propose a technological approach based on a mixed-conductive CO₂ permeable membrane reactor (i.e., MOCC membrane) to realize the efficient conversion of CH₄ and the capture and resourceful utilization of CO₂. The membrane reactor used a dual-phase membrane composed of samarium-doped ceria (SDC) and lithium-sodium eutectic carbonate (MC) when loaded with the LaNi_0.8Cu_0.2O_3-δ (LNC) catalyst, significantly enhancing the CO₂ permeation flux and the catalytic performance of the DRM reaction.

A dual-phase MOCC membrane composed of samarium-doped ceria (SDC) and lithium-sodium binary eutectic carbonate (Li_0.52Na_0.48)₂CO₃ was fabricated. The SDC porous matrix was synthesized via coprecipitation and subsequent impregnation with molten carbonate to form a dense structure. A Cu-doped LaNiO₃ perovskite catalyst (LaNi_0.8Cu_0.2O_3-δ) was prepared by a coprecipitation method and loaded onto the membrane reactor. The membrane's CO₂ permeation flux was evaluated under simulated flue gas and SOFC anode exhaust conditions. The catalytic performance, including CH₄ conversion, H₂/CO production rates, and stability, was systematically tested at 650-850 ℃. The samples were characterized by X-ray diffraction (XRD), scanning electron microscopy (SEM), and gas chromatography, respectively.

The catalytic performance of LaNi_1-xCu_xO_3-δ (LNC) catalysts with varying Cu doping levels (x = 0, 0.2, 0.4, 0.6) is systematically evaluated in a fixed-bed reactor for methane dry reforming (DRM). At 850℃, LaNi_0.8Cu_0.2O_3-δ catalyst exhibits the maximum CH₄ conversion rate (i.e., 99.8%) and CO₂ conversion rate (i.e., 98.4%), along with optimal H₂ and CO production rates of 1.36 and 1.50 mL·min^-1, respectively. In contrast, undoped LaNiO₃ catalyst shows inferior activity (i.e., CH₄ conversion: ~85%), highlighting the critical role of Cu doping in enhancing catalytic performance. The improved activity is attributed to Cu incorporation promoting oxygen vacancy formation and lattice oxygen mobility, suppressing carbon deposition and enhanced reaction kinetics. Note that the excessive Cu doping (x ≥ 0.4) leads to reduced activity due to the partial blockage of active sites and structural instability, underscoring the importance of balanced Cu substitution.

The dual-phase mixed oxygen and carbonate ionic conductor (MOCC) membrane, composed of SDC and lithium-sodium eutectic carbonate (Li_0.52Na_0.48)₂CO₃, has robust CO₂ permeation capabilities. Under non-reactive conditions, the CO₂ flux increases from 0.27 to 0.90 mL·cm^-2·min^-1 as the temperature increases from 650 to 850 ℃, with an activation energy of 51.93 kJ·mol^-1, indicating a thermally driven permeation mechanism. When coupled with DRM, the CO₂ flux surges to 1.52 mL·cm^-2·min^-1 at 850 ℃, driven by the enhanced CO₂ partial pressure gradient resulting from continuous CO₂ consumption in the reaction. This synergy between CO₂ capture and conversion significantly outperformes conventional fixed-bed reactors, where CO₂ utilization is limited by equilibrium constraints.

In the integrated membrane reactor loaded with LaNi_0.8Cu_0.2O_3-δ, the exceptional DRM performance is achieved under simulated flue gas (i.e., 60% N₂-40% CO₂) and SOFC anode exhaust (i.e., 40% CO₂, 2% H₂, 2% CO) conditions. At 850 ℃, CH₄ conversions reach 97.31% and 95.51%, respectively, with CO and H₂ production rates of 2.39 and 1.44 mL·cm^-2·min^-1 (flue gas) and 2.93 and 1.38 mL·cm^-2·min^-1 (SOFC exhaust). The H₂/CO ratio (i.e., ~0.6-0.7) deviates slightly from the stoichiometric value of 1, likely due to the reverse water-gas shift (RWGS) reaction at elevated temperatures. The results of long-term stability tests at 825 ℃ CH₄ conversion (i.e., ~97%) or syngas production rates, indicating the system's robustness. The analysis of SEM images and XRD patterns indicate the absence of carbon deposits and preserved catalyst phase structure, thus validating the anti-coking properties of the Cu-doped perovskite and the membrane's thermal stability.

Compared to the existing studies, this work develops a membrane reactor technology via achieving higher CO₂ permeation fluxes and catalytic efficiencies. LaNi_0.8Cu_0.2O_3-δ catalyst has a higher activity with a prolonged stability. Furthermore, the dual-phase membrane's unique ion-conduction mechanism circumventes the trade-off between selectivity and permeability in conventional membranes, offering a scalable solution for industrial CO₂ capture and utilization. These results indicate a potential of integrating advanced perovskite catalysts with MOCC membranes to achieve efficient, stable, and economically viable DRM systems.

This work presented a breakthrough in coupling CO₂ capture with DRM using a MOCC membrane reactor. When loaded with LaNi_0.8Cu_0.2O_3-δ catalyst, the membrane reactor could enhance the CO₂ permeation flux and the catalytic performance of the DRM reaction. At 850℃, employing the LaNi_0.8Cu_0.2O_3-δ catalyst, methane conversion rates achieved were 97.31% and 95.51% for simulated flue gas and SOFC anode off-gas, respectively. Correspondingly, CO₂ conversion rates were 98.34% and 78.49%, while the production rates of CO were 2.39 and 2.93 mL·cm^-2·min^-1, and those of hydrogen were 1.44 and 1.38 mL·cm^-2·min^-1, respectively. The results of long-term stability tests indicated that the membrane reactor had a stable performance for over 60 h, demonstrating promising application prospects. The technology could reduce CO₂ emissions and convert waste gases into valuable syngas, aligning with global carbon-neutral goals. A future research could focus on scaling up the reactor and optimizing operational parameters for broader implementation.

Conducting in-depth research and taking measures to mitigate Cr poisoning on the cathode materials is crucial for further advancing the commercialization of SOFCs technology. In this review, recent development in enhancing the Cr tolerance of cathodes is represented. The theoretical mechanisms of Cr deposition on cathodes are introduced, and the reported strategies to alleviate Cr poisoning on cathodes are summarized. Despite the significant progress made in the existing research, there are still some challenges to be addressed, i.e., a) it seems that a single theory cannot perfectly explain the Cr deposition on different cathode materials. For different materials under different test conditions, these mechanisms may occur simultaneously or compete with each other. In addition, in proton-conducting SOFCs (H-SOFCs), these processes may be more complicated due to the introduction of protons. Although some researchers deal with the problem of Cr poisoning in H-SOFCs, there are no detailed literature reports on the mechanism of Cr poisoning in H-SOFCs system; b) Redesigning or improving the currently commercialized interconnect materials faces high costs. Applying a protective coating on the interconnects is a feasible approach. However, the added cost of additional manufacturing processes also needs to be considered; c) The surface modification of cathodes can effectively strengthen its Cr resistance. However, isolated nanoparticles are unable to achieve complete coverage of the inherently fragile electrodes. The areas of the cathode surface that are not covered may be still poisoned by contaminants such as CO₂, Cr vapor, and steam. Moreover, if the impregnated surface catalysts are used as a preferred reactant of the gaseous Cr species, they may be continuously consumed for long periods of operation. Although the poisoning effect of the deposits is mild, excessive accumulation of the deposits will occupy the active sites for the oxygen reduction reaction and hinder the diffusion of gases in the cathode; d) The design of contaminants-tolerant high-entropy materials needs to balance electrocatalytic activity and stability. In addition, the interaction mechanisms of different metal cations in the high-entropy cathodes are still unclear and require further in-depth research; and e) Recent progress has been made in the application of SOFCs in electrolysis mode. As is known, the electrode material on the air side undergoes cathodic polarization in fuel cell mode, while in electrolysis mode, anodic polarization occurs on the electrode on the air side. Therefore, the mechanisms and degree of Cr poisoning will be different. Unfortunately, there is still a lack of relevant research on Cr deposition in electrolysis mode. In summary, the phenomenon of Cr poisoning in materials is a long-standing challenge for SOFCs and other high-temperature electrochemical devices. A future research should focus on the investigation on Cr poisoning mechanisms under various operating modes and optimization of the composition and structure of cathode materials. These efforts aim to enhance the stability and reliability of SOFCs in practical industrial applications, ultimately advancing the commercialization process of SOFCs technology.

With the continuous expansion of infrastructure construction in alpine regions, a demand for concrete construction under sub-zero temperatures increases significantly. However, conventional low-temperature construction methods suffer from high energy consumption and complex operational processes. Although sulfoaluminate cement (SAC) exhibits excellent low-temperature adaptability, and calcium chloride (as an antifreeze agent) can effectively lower the freezing point and maintain a liquid-phase environment, the hydration kinetics of the simple SAC-calcium chloride composite system under fully cold construction conditions (≤-15 ℃) are severely inhibited at sub-zero temperatures, leading to an insufficient early-age strength development, which fails to meet the rapid construction requirements of engineering projects. Consequently, there is an urgent need to optimize this composite system to fully exploit its rapid hardening and early-strength characteristics under fully cold conditions at -15 ℃.

Anhydrite as a key component of SAC critically regulates the composition of hydration products, microstructure, and macro-scale performance of the cementitious system. However, the existing studies on the effect of anhydrite dosage primarily focus on ambient temperatures or relatively mild sub-zero conditions (e.g., >-5 ℃). Systematic investigations into how anhydrite dosage governs the hydration product evolution, microstructural formation, and mechanical-deformation properties (particularly early-age performance) of the SAC-calcium chloride composite system under extreme low-temperature conditions (-15 ℃) and fully cold construction processes remain largely unexplored.

This study was to systematically reveal the critical regulatory effects and intrinsic mechanisms of anhydrite dosage on the low-temperature hydration and hardening behavior of the SAC-calcium chloride composite system under fully cold construction conditions at -15 ℃, simulating the harsh environments encountered in real-world engineering. The findings could be expected to expand the application potential of SAC in extreme environments, particularly in remote regions lacking thermal energy supply.

Under fully cold construction conditions (chilled materials, mixing, and curing) at -15 ℃, a composite system was designed with SAC clinker and anhydrite as binders and a 20% calcium chloride solution as a mixing medium. Anhydrite dosage gradients were set at 0%, 5%, 10%, 15%, 20%, 25%, and 30%, respectively.

The mortar specimens (40 mm × 40 mm × 160 mm) were prepared at a water-to-binder ratio of 0.37 based on the standard GB/T 17671—2021 Test Method for Cement Mortar Strength (ISO Method) for strength evaluation. The shrinkage specimens (40 mm × 40 mm × 160 mm) were prepared based on the standard JGJ/T70—2009 for Test Methods of Basic Properties of Construction Mortar.

Cement paste specimens were formulated at a water-to-binder ratio of 0.32. The calcium chloride solution and cement were sequentially poured into a mixer, stirred at a low speed for 120 s, paused for 15 s, and then stirred at a high speed for 120 s. The resultant mixture was cast into molds and compacted by a vibrating table for 60 cycles. All the specimens were cured on racks under uncovered conditions at -15 ℃.

After reaching specified curing ages, the mortar specimens underwent macroscopic tests. Cement paste specimens were crushed on-site, submerged in anhydrous ethanol to terminate hydration at room temperature for ≥7 d, and then vacuum-dried at 40 ℃ and -0.08 MPa for ≥24 h. The dried samples were subjected to the microstructural analyses to investigate the phase composition and hydration mechanisms.

Under fully cold construction conditions at -15 ℃, the incorporation of 10% anhydrite dosage enables the SAC-calcium chloride composite system to achieve the 1-d and 3-d compressive strengths of 20.1 MPa and 38.0 MPa, respectively, representing approximately 100% enhancement, compared to the pure clinker group. At an anhydrite dosage of 15%, the peak hydration temperature increase reaches 18.9 ℃ (33.9 ℃ relative to ambient temperature), effectively addressing the challenges of delayed early hydration kinetics and insufficient strength in sub-zero environments.

Anhydrite significantly suppresses a shrinkage via promoting the formation of expansive AFt phases. At the dosage of 5%, the 3 d shrinkage rate reduces to 0.100% (i.e., 47.4% reduction), while at the dosage of 25%, the 28 d shrinkage rate decreases to 0.237% (i.e., 35.1% reduction), offering a graded solution for a low-temperature shrinkage control.

The microstructural analyses reveals that anhydrite regulates the types and morphology of hydration products. In the 28 d hydrated pure SAC clinker, unstable petal-like Friedel's salt crystals occur. Anhydrite optimizes the Cl/S ratio of the system, promoting AFt formation, while suppressing Friedel's salt generation. At the optimal dosage of 10%, needle/rod-shaped AFt crystals form a dense interlocking network, which is pivotal for early-age strength enhancement. However, the excessive dosage (>10%) leads to unreacted anhydrite enrichment and short rod-shaped AFt aggregates with localized bridging, resulting in the strength regression at later ages.

Under fully cold construction conditions at -15 ℃, anhydrite significantly enhanced the hydration activity and early-age strength of the SAC-calcium chloride composite system. An appropriate anhydrite dosage of 10% promoted the hydration process of calcium sulfoaluminate in the system and accelerated the nucleation and growth rate of AFt, thereby forming a denser microstructure of early hydration products. However, the excessive anhydrite disrupted the sulfate phase equilibrium in the reaction system, inhibited the continuous formation of AFt, and induced anhydrite enrichment, ultimately degrading the mechanical properties due to structural loosening.

At early ages, the anhydrite dosage of 5% approached the optimal sulfate balance required for hydration, effectively compensating for plastic shrinkage and chemical shrinkage. In contrast, the dosage of 25% provided sufficient SO₄^2- ions during later hydration stages, ensuring sustained AFt formation and suppressing drying shrinkage over time.

Anhydrite optimized the Cl/S molar ratio in the system, facilitating the formation of a dense network of needle-bar Aft, while inhibiting the formation of the unstable Friedel's salt phase. The excessive anhydrite, however, led to interconnected short-rod AFt and gypsum enrichment, further compromising the structural integrity.