Rare-earth ion-doped materials demonstrate outstanding advantages in solar-blind photodetection due to their unique energy level structure, efficient energy transfer, and controllable luminescence properties. Remarkable progress is made in material design, energy transfer mechanism clarification, matrix modification, defect engineering, nanostructure construction, and device performance optimization. The optimized devices exhibit enhanced responsivity, widened spectral response, faster response speed, lower dark current, and improved stability, showing broad application prospects in military, civil, environmental, and biomedical fields. Nevertheless, several critical scientific and technical challenges still hinder their practical deployment. For instance, the trade-off between high energy transfer efficiency and long-term structural stability remains difficult to balance. The excessive rare-earth doping often causes concentration quenching and luminescence attenuation. A precise control over microstructures, interfaces, and defect states remains challenging, and the dynamic photophysical evolution under operating conditions requires a further in-depth verification via in-situ characterization techniques.

Future research directions of rare-earth-based solar-blind photodetection will focus on the development of novel composite material systems via integrating rare-earth dopants with two-dimensional materials, perovskites, and other emerging functional media to construct high-efficiency energy transfer channels. In the device level, developing miniaturized, integrated, and intelligent micro-/nano-solar-blind photodetectors combined with MEMS technology becomes a major trend. Meanwhile, theoretical simulations based on first-principles calculations, high-throughput material screening, and low-cost scalable fabrication processes should be strengthened to accelerate the industrial translation of laboratory achievements. This review provides a systematic and valuable reference for the rational design, performance optimization, and practical innovation of high-efficiency rare-earth-doped solar-blind photodetection materials and devices.

SOFC research shifts from single-cell materials to stack-level system integration. The experimental evidence shows that the contact between critical stack components is a dominant bottleneck governing both power output and lifetime. The anode side, operating in a reducing atmosphere and forming a metal-to-metal contact, exhibits a contact resistance, which is five orders of magnitude lower than the oxide-to-oxide interface on the cathode side and can be therefore neglected. The cathode side, in contrast, must rely on a current-collector/coating system that simultaneously ensures electron collection, stress buffering and oxidation protection. Consequently, future interface optimization will revolve around a three-dimensional, "current-collector material, interconnect coating and surface roughness" synergistic design framework.

Current-collector development evolves from noble metals to oxides and onward to graded, dual-phase composites. These systems aim to deliver conductivities on the order of kilosiemens/cm, while achieving triple matching-thermal, mechanical and chemical-with both the cathode and the interconnect through coordinated control of composition, microstructure and porosity.

Meanwhile, an accurate quantification of interfacial resistance remains a critical challenge. Conventional four-point measurements are limited by stack hermeticity, yielding only the total resistance, making it impossible to isolate the true interfacial contribution. The next step involves embedding ultrathin leads within the stack to couple AC impedance spectroscopy with in-situ voltage monitoring, thereby tracking the interfacial state of every repeating unit in real time. Post-mortem laser confocal microscopy and atomic force microscopy will be employed to establish quantitative correlations among surface roughness, contact depth and power degradation, creating a data-closed loop for predictive interface engineering.

The existing interface tuning still relies heavily on trial and error, and outcomes remain unpredictable. Understanding interfacial mechanisms can favor the design of SOFC stacks to lock in optimal clamping pressures, roughness windows and material combinations, thereby achieving a precise performance control. This mastery is essential to realizing commercial durability targets of tens of thousands of hours and laying the foundation for large-scale deployment in distributed generation.

Lithium-ion and sodium-ion batteries underpin portable electronics, electric vehicles, and grid-scale energy storage. Their performance and safety are strongly constrained by cathode behavior, and practical screening repeatedly requires three types of predictions, i.e., voltage profiles during (de)intercalation, alkali-ion migration kinetics, and thermal stability against oxygen release and decomposition. Density functional theory (DFT) can provide accurate baselines, but its cost limits supercell sizes, configuration sampling, and the time/length scales accessible to ab initio molecular dynamics (AIMD). Pretrained machine-learning interatomic potentials (MLIPs) offer near-DFT accuracy at far lower cost, thus enabling high-throughput evaluation and long-time molecular dynamics. However, the fidelity required for voltage thermodynamics, migration kinetics, and high-temperature decomposition is not identical, and a model that performs well on one task may be unreliable on another. In this study, eight representative pretrained MLIPs (i.e., MACE, M3GNet, CHGNet, ALIGNN, SevenNet, AlphaNet, GRACE, and Orb) were systematically benchmarked across these three cathode-relevant tasks under matched protocols.

All crystallographic prototypes were obtained from the Materials Project. All the MLIPs were used as released pretrained models without fine-tuning to reflect a "drop-in" screening scenario. For voltage profiles, four representative cathodes spanning layered oxides and polyanion frameworks were selected, i.e., NaMnO₂, LiCoO₂, NaFePO₄, and Na₃V₂(PO₄)₃. Each parent structure was expanded to a supercell containing 8-12 alkali sites. Partially (de)intercalated configurations were generated by exhaustive enumeration of alkali-vacancy patterns and symmetry-deduplicated with a space-group analysis tool. Each MLIP evaluated energies for all configurations. Formation energies were referenced to alkali-rich/poor endmembers, and lower convex hulls were constructed to obtain piecewise average voltages. Accuracy and curve-shape fidelity were quantified using metrics including mean absolute error (MAE), root mean square error (RMSE), integrated absolute error (IAE), and bias indicators.

For ion migration, Li₃Sc₂(PO₄)₃ was chosen as a representative fast-ion conductor. Molecular dynamics was performed at 600 K for 2 ns with each MLIP, and the Li self-diffusion coefficient was extracted from the mean-square displacement (MSD) via the Einstein relation in three dimensions. A fixed regression window (200-1500 ps) was applied consistently to reduce transient and finite-sampling effects.

For thermal stability, oxygen-release/decomposition was benchmarked on phosphate systems with clear stepwise pathways, i.e., MnPO₄ and FePO₄ in olivine and trigonal polymorphs. Each step was represented by balanced solid-state reactions with explicit O₂ release. Reaction energies from MLIPs were combined with an ideal-gas oxygen chemical potential in an oxygen grand-potential framework to estimate onset temperatures and cumulative O₂-evolution curves.

The benchmark reveals a pronounced task dependence among pretrained MLIPs. For voltage profiles, most models reproduce the qualitative multi-plateau behavior, yet quantitative accuracy differs because voltages are sensitive to small energy differences among near-degenerate vacancy orderings that determine convex-hull vertices and plateau boundaries. Across the four cathodes, M3GNet achieves the minimum overall voltage error with a small systematic bias, followed by AlphaNet and CHGNet. GRACE is generally mid-tier, whereas Orb and ALIGNN exhibit larger offsets and shape errors. A notable system dependence occurs for LiCoO₂, where most MLIPs tend to underestimate voltages relative to the reference, indicating that layered Co-O chemistry remains a challenging regime for the existing universal pretrained models.

For ion migration in Li₃Sc₂(PO₄)₃ at 600 K, the ranking differs from the voltage benchmark. MACE and SevenNet yield diffusivities closest to the reference, with Orb and GRACE moderately higher. CHGNet and M3GNet overestimate a diffusivity by severalfold, while AlphaNet underestimates it more strongly. Importantly, ALIGNN can not reliably complete the long-timescale molecular-dynamics runs under our resource constraints, highlighting a practical limitation (memory footprint) that can matter in screening pipelines. These support the interpretation that diffusion is governed primarily by local force accuracy and barrier-region smoothness along hopping pathways, whereas voltage profiles depend on consistent ranking of many competing configurations across composition.

For thermal stability, all the MLIPs qualitatively reproduce the existence of stepwise oxygen evolution and pyrophosphate-forming decomposition, but predicted onset temperatures can deviate substantially. For MnPO₄, deviations span a wide range. ALIGNN and M3GNet provide the smallest deviations for this system, while AlphaNet and CHGNet delay oxygen release. Across the full phosphate set, M3GNet and MACE deliver the optimum overall agreement with experimental step positions and temperatures, and GRACE often captures intermediate steps with moderate errors. The results indicate that generalization to high-temperature, oxygen-deficient pathways remains sensitive to both training coverage and architectural bias.

This work established a unified, extensible benchmark for comparing pretrained MLIPs on cathode-relevant thermodynamics, kinetics, and high-temperature stability. No single MLIP could be universally optimal. M3GNet was most reliable for voltage prediction on the tested cathodes, MACE and SevenNet were strongest for long-time MSD-based diffusion in Li₃Sc₂(PO₄)₃, and M3GNet together with MACE best captured oxygen-release/decomposition trends in representative phosphate systems. The proposed workflow could provide a practical guidance for task-aware MLIP selection and a foundation for larger, more decoupled benchmarks in future studies.

AI achieves notable progress in polymer functional materials, particularly in inverse design, performance prediction, and process optimization, accelerating the shift from experience-driven to data-driven research. To fully unlock AI's potential, some challenges in data, algorithms, and integration must be systematically addressed. This review represents a dedicated polymer database, a functional unit-based encoding method, and an interpretable structure-performance framework to bridge the gap between "black-box" model outputs and human-understandable chemical insight. Four key directions for future work should be concerned, i.e., 1) building comprehensive, open, and interoperable polymer databases; 2) advancing generative and reinforcement learning for autonomous material discovery; 3) strengthening the dynamic coupling between experiments and models to form self-driving research loops; and 4) fostering interdisciplinary collaboration and integrated platform development. AI can evolve from a supportive tool into a core innovative engine for polymer functional materials, powered by the synergy of data, algorithms and experiments.

Glass fiber reinforced cement is utilized in construction field. Interfacial modification with coupling agents and functional polymers represents a critical strategy to enhance interfacial bonding. However, molecular mechanisms remain insufficient. In this study, molecular dynamics were used to evaluate interfacial responses of C-S-H/glass fiber modified with KH-570 and poly (vinylpyrrolidone-co-acrylic acid) (PVP-co-PAA). The results demonstrated that KH-570 induced marginal increase, while PVP-co-PAA led to remarkable enhancement. The analyses of coordination number, bond lifetime decay decoded interfacial bonding networks before and after modification. This study could reveal the distinct failure pathways and molecular mechanisms of interfacial bonding.

All the MD simulations were performed based on a package named LAMMPS. Firstly, all the systems were relaxed under NVT ensemble last for 5 ns, with timestep 1 fs and 300 K. Temperature control was achieved by Nose-Hoover thermostat and damping parameter 0.1 ps. The bottom Ca layers of C-S-H were fixed throughout the simulation to prevent model rotation. An additional 2 ns relaxation was conducted and trajectories were recorded every 1 ps. During the shear simulations, spring forces were applied on atoms located at the top of SiO₂ slab.

The molecular dynamics (MD) simulations are employed to evaluate shear mechanical properties of C-S-H/SiO₂, C-S-H/KH-570 and C-S-H/PVP-co-PAA interfaces. The molecular mechanisms of interfacial modification are thoroughly revealed via analyzing the types and dynamic behaviors of interfacial bonding networks. During dynamic failure, PVP-co-PAA exhibits a distinct behavior compared with rigid SiO₂. Flexible polymer networks undergo conformational changes, leading to an increased shear displacement. The density analyses of bonding networks indicates that interfacial bonding networks can reorganize from O_SiO2 —Ca—O_C-S-H into O_KH-570/O_PVP-co-PAA—Ca—O_C-S-H. Moreover, interfacial failure is decided by ionic bonding of O_SiO2 /O_KH-570/O_PVP-co-PAA—Ca. The coordination number follows an increasing order of O_SiO2 <O_KH-570<O_PVP-co-PAA, explaining the differences of interfacial mechanical strength.

The MD simulation revealed that PVP-co-PAA modification showed the most enhancement, with an improvement of 302.7%. The coordination number followed an increasing order of O_SiO2 <O_KH-570<O_PVP-co-PAA. The time correlation function (TCF) also revealed that interfacial stability was enhanced after modification. Based on the coordination number and the TCF results, the differences of interfacial mechanical strength were explained. These findings could provide fundamental insights to guide the functional design of fiber-cement interfaces.

The construction of transportation infrastructure in plateau regions, such as the Sichuan-Tibet Railway and the Xinjiang-Tibet Railway, China, is progressing rapidly under the national development strategies. The annual minimum temperature in Tibet can reach -45 ℃, and the number of days with alternating positive and negative temperatures accounts for more than half of the year, forming an extreme low-temperature, high-frequency freeze-thaw environment. Furthermore, structures such as bridges, culverts, and tunnels in plateau areas are often subjected to erosion from de-icing salts or chlorides in the soil. The combined action of freeze-thaw and chloride attack poses a serious threat to the durability of concrete structures. Fiber-reinforced polymer composites, such as carbon fiber reinforced polymer (CFRP), basalt fiber reinforced polymer (BFRP), and glass fiber reinforced polymer (GFRP) bars, are widely used in corrosive environments like coastal and saline areas due to their high strength and corrosion resistance. The bond performance of the steel/FRP bar-concrete interface significantly affects the mechanical behavior of concrete structures. However, the existing research mostly focuses on the room-temperature or conventional freeze-thaw environments, and the understanding of the degradation mechanism of the bar-concrete bond performance under the combined action of low-temperature freeze-thaw and chloride attack specific to plateau regions remains insufficient. It is thus necessary to conduct a targeted research on the bond performance of the steel/FRP bar-concrete interface under low-temperature freeze-thaw and chloride attack environments in the Tibetan plateau.

A total of 144 pull-out specimens were fabricated. The test parameters included bar type (i.e., steel, BFRP, CFRP, and GFRP bars), bar diameter (i.e., 10, 16 mm, and 20 mm), and the number of freeze-thaw cycles (i.e., 0, 50, 100, and 150). After 28 d standard curing, the specimens were first subjected to a 4 d water saturation pretreatment to ensure that they reached a saturated state before the freeze-thaw cycle test. A programmable high-low temperature test chamber was used to simulate a freeze-thaw cycling process. Each freeze-thaw cycle lasted for 260 min (i.e., consisting of 180 min of freezing and 80 min of thawing). After every 5 freeze-thaw cycles, the specimens were placed at 20 ℃ and sprayed with a NaCl solution to maintain a stable moisture content. Following the designated freeze-thaw cycles, the specimens were immersed in a 5% NaCl solution for 15 d to accelerate chloride ingress. Finally, the central pull-out tests were conducted by a 300 kN MTS testing machine at a loading rate of 0.5 mm/min, with the free-end slip measured by a displacement transducer at a data acquisition frequency of 10 Hz.

The failure modes of the specimens are primarily governed by bar type and diameter, with freeze-thaw cycles showing negligible influence. All the steel bar specimens exhibit a pull-out failure accompanied by longitudinal cracks, with crack width increasing alongside bar diameter. The GFRP bar specimens also fail due to pull-out without concrete cracking. In contrast, for the BFRP and CFRP bars, the failure mode transitions from pull-out to splitting failure when the diameter increases from 10 mm to 16 mm. The bond strength decreases with increasing bar diameter for all bar types. When the diameter increases from 10 mm to 20 mm, the bond strength reduction for steel bars (i.e., 51.7%-56.3%) is significantly greater than that for FRP bars (i.e., below 18.2%). After 150 freeze-thaw cycles, the bond strength of steel bars is decreased by more than 31.4%, while the reduction for BFRP bars does not exceed 22.1%. The degradation mechanisms differ between steel and FRP bars. For steel bars, the bond degradation is mainly attributed to concrete deterioration and steel corrosion induced by the coupled environment. For FRP bars, in addition to concrete deterioration, the degradation involves resin matrix damage from freeze-thaw cycles and the formation of interfacial gaps due to the mismatch in thermal expansion coefficients between FRP and concrete. For peak slip, steel bar specimens exhibit the values between 1.6 mm and 2.5 mm, which are considerably lower than those of FRP bar specimens (i.e., ranging from 2.7 mm to 4.1 mm). As the diameter increases from 10 mm to 20 mm, the peak slip is increased by 5.0%-13.3% for all the specimens. Conversely, as freeze-thaw cycles increase from 0 to 150, the peak slip is decreased by 13.5%-23.8%. Note that no significant interaction effect between bar diameter and freeze-thaw cycles on peak slip occurs. Based on the experimental data, the prediction models for bond strength and peak slip are proposed through normalization, incorporating the effects of freeze-thaw cycles and bar diameter. The data by the models are in reasonable agreement with the experimental results, with coefficients of determination (R²) of exceeding 0.86.

This study investigated the bond performance of steel and FRP bars with concrete under low-temperature freeze-thaw and chloride attack. The failure mode was primarily determined by bar type and diameter. The bond strength decreased with increasing diameter, and steel bars had a more pronounced reduction than FRP bars. The freeze-thaw cycles significantly reduced the bond strength for all bar types, the underlying degradation mechanisms differed between steel and FRP bars. The peak slip increased with diameter but decreased with more freeze-thaw cycles, with no significant interaction between these two factors. The proposed prediction models, which could account for freeze-thaw cycles and normalized bar diameter, effectively captured the degradation of bond strength and peak slip, providing a valuable tool for durability design and assessment of concrete structures in harsh plateau environments.

The rapid development and practical deployment of hyperspectral detection technology render conventional camouflage materials increasingly inadequate for covert protection in complex forest environments, primarily due to their insufficient spectral matching and limited functionality. A critical challenge in forest camouflage lies in the accurate replication of four characteristic spectral signatures of natural vegetation, i.e., the green peak, the red edge, the near-infrared plateau, and the near-infrared water absorption peak. These features form the unique spectral "fingerprint" of vegetation, which serves as a fundamental basis for evading multi-band, high-precision detection. Among them, the green peak governs a visual concealment within the visible region, while the near-infrared water absorption peak acts as a decisive marker for distinguishing vegetation from artificial materials, which are essential for effective camouflage. However, the existing forest camouflage paints and simulation materials are constrained by inadequate structural design and limited functional integration. Most commercially available products can only partially mimic certain spectral traits of vegetation and commonly exhibit deficiencies in core performance. Note that it remains particularly difficult to simultaneously and accurately match both the green peak of healthy foliage and the near-infrared water absorption peak. This shortfall makes such materials susceptible to rapid identification under hyperspectral imaging, thereby severely limiting the practical effectiveness of the existing forest camouflage technologies. Consequently, there is an urgent need for the research and development of novel camouflage materials capable of comprehensive spectral simulation.

Six types of sulfate intercalated Mg/Cr layered double hydroxides (LDHs) were synthesized by a coprecipitation method. The crystalline structure of the as-prepared materials was examined by X-ray diffraction (XRD). The molecular structures and characteristic absorption features were determined by Fourier-transform infrared spectroscopy (FT-IR). The thermal decomposition behavior and mass loss profiles were analyzed by thermogravimetry-differential thermal analysis (TG-DTA). The surface morphology and particle size distribution were characterized by scanning electron microscopy (SEM). These characterization techniques provided a comprehensive structural and physicochemical profile of the synthesized LDHs. Subsequently, to meet the requirement of reproducing the green spectral peak in jungle camouflage, a functional camouflage coating was fabricated via blending the optimized LDHs material with chromium-based green pigment. This formulation enhanced the green-peak characteristics in the visible region and preserved the pronounced water-absorption peak in the near-infrared range. The spectral performance of the coating was evaluated by visible-near-infrared spectroscopy (Vis-NIR), and its thermal camouflage capability was assessed by infrared thermographic imaging.

The results systematically indicate that a series of chromium-containing hydrotalcite materials, prepared by a controlled synthesis process, exhibit typical crystalline structural characteristics of layered double hydroxides (LDHs). The XRD patterns reveal sharp and symmetric diffraction peaks, with the characteristic peaks corresponding to the layered structure displaying a high intensity and a regular shape, indicating a good crystallinity and a well-ordered interlayer arrangement. Among the series of chromium-containing hydrotalcites, sulfate-intercalated magnesium chromium hydrotalcite (MgCr-SO₄^2--LDHs) demonstrates unique structural advantages, i.e., its interlayer spacing is significantly larger than that of other intercalated types of magnesium chromium hydrotalcites. Simultaneously, The TG-DTA thermal analysis indicates that this material exhibits the maximum mass loss of 26.38% at 25-400 ℃. This is directly related to the content of water molecules stored within the interlayers. The spatial configuration and charge distribution characteristics of the sulfate intercalation ions provide a sufficient space for the stable adsorption and storage of water molecules. As a result, MgCr-SO₄^2--LDHs possesses the most abundant interlayer water content among the prepared samples. This rich interlayer water constitutes the core structural basis for simulating the near-infrared water absorption peak of vegetation. The visible to near-infrared spectra (400-2500 nm) further reveal the optical properties of the Mg/Cr hydrotalcite. In the visible region, the material shows a distinct characteristic absorption peak at 490 nm (blue region), attributed to its intrinsic electronic transition behavior. In the near-infrared region, intense and sharp water absorption peaks clearly occur at approximately 1400 nm and 1900 nm, showing a high similarity to the near-infrared water absorption features of natural vegetation leaves. Sulfate-intercalated magnesium chromium hydrotalcite (MgCr-SO₄^2--LDHs) is modified with chromium(III) oxide (Cr₂O₃) by an in-situ coating process via leveraging these characteristics. The near-infrared water absorption properties imparted by the abundant interlayer water in MgCr-SO₄^2--LDHs were combined with the green optical characteristics of Cr₂O₃. This complementary interaction successfully offset the influence of the intrinsic blue absorption peak at 490 nm from the magnesium chromium hydrotalcite. Ultimately, a jungle camouflage coating simulation material is prepared, having both green visual characteristics and distinct near-infrared water absorption peaks. This provides a key material foundation for subsequent high-similarity spectral matching with natural vegetation.

The camouflage coating fabricated with an optimal MgCr-SO₄^2--LDHs@Cr₂O₃ : MgCr-SO₄^2--LDHs ratio of 3 : 7 could enable a precise spectral matching with natural vegetation leaves. It accurately replicated both the green peak and the near-infrared water absorption peak, achieving a spectral similarity of up to 95.80%. Furthermore, the results of thermal imaging tests revealed no significant difference between the coating and natural vegetation. This study on dual-functional materials that simulated color and the near-infrared water absorption peak could thus offer a promising direction for the development of advanced vegetation camouflage technologies.

Commercial ternary cathode materials have their theoretical performance limits. Consequently, enhancing energy density, reducing costs, and improving cycling stability without compromising safety are critical challenges for both academia and industry. Among the existing candidates, LiNi_0.9Mn_0.1O₂(NM91) offers a significant potential due to its high specific capacity, cost-effectiveness, and low-cobalt (or cobalt-free) nature. However, ahigh nickel content induces severe structural instability. Elevated Ni levels exacerbate Li⁺/Ni²⁺ cation disordering, thus disrupting the α-NaFeO₂-type layered structure and impeding lithium-ion de/intercalation kinetics, which degrades a rate capability. Furthermore, during high-voltage cycling (>4.3 V), detrimental interfacial reactions occur, i.e., electrolyte decomposition, transition metal dissolution, and the formation of Ni-rich rock-salt or amorphous phases. These degradation mechanisms destabilize the electrode-electrolyte interface, accelerate capacity fade, exacerbate electrode polarization, and severely compromise cycling longevity and battery safety. To address these challenges, this study was to propose an innovative Mg/Nb/Ti co-modification strategy to enhance the structural stability and electrochemical performance of single-crystal LiNi_0.9Mn_0.1O₂ cathodes.

The Ni_0.9Mn_0.1(OH)₂ precursor was first homogeneously blended with LiOH·H₂O and flux under strictly controlled stoichiometric conditions (i.e., at a Li : (Ni+Mn) molar ratio of 1.05∶1.00 and a (LiCl+KCl) ∶ (Ni+Mn) mass ratio of 0.3 ∶ 1.0). The mixture was then calcined in a flowing oxygen atmosphere, heated to 550 ℃ at 3 ℃/min (300 min hold), ramped to 900 ℃ at the same rate for 60 min, cooled controllably at 5 ℃/min to 820 ℃ for 840 min, and finally cooled to ambient temperature, yielding a phase-pure single-crystal LiNi_0.9Mn_0.1O₂ (designated SC-NM91).

For the doped samples, Ni_0.9Mn_0.1(OH)₂ precursor was homogenized with LiOH·H₂O, Mg(NO₃)₂, and C₁₀H₅NbO₂₀·xH₂O in anhydrous ethanol under vigorous agitation. C₁₆H₃₆O₄Ti was added in dropwise, followed by continuous stirring and drying at 60 ℃ until complete solvent evaporation. The resultant mixture had a controlled stoichiometry of Li ∶ (Ni+Mn) ∶ Mg ∶ Nb ∶ Ti = 1.05 : (1-x-y-z) ∶ x ∶ y ∶ z (x=0.005, 0.010, 0.020; y=0.002 5, 0.005 0, 0.010 0; z=0.01).

The identical solid-state sintering protocol used for SC-NM91 was applied to synthesize Mg/Nb/Ti tri-doped LiNi_0.9-x-y-zMn_0.1Mg_xNb_yTi_zO₂ cathodes with controlled dopant gradients. The compositions of SC-NM91-0.5Mg@0.25Nb@1Ti, SC-NM91-1Mg@0.5Nb@1Ti, and SC-NM91-2Mg@1Nb@1Ti were produced via unified thermal processing.

Among the modified cathodes, SC-NM91-0.5Mg@0.25Nb@1Ti demonstrates significantly enhanced cycling stability and superior overall electrochemical performance, compared to SC-NM91-1Mg@0.5Nb@1Ti and SC-NM91-2Mg@1Nb@1Ti.

The XRD patterns reveal a systematic peak shift toward lower angles in the modified samples relative to SC-NM91, indicating a lattice expansion along the c-axis induced by elemental doping. SC-NM91-0.5Mg@0.25Nb@1Ti exhibits enhanced cationic ordering with an R-factor of 1.749 0 versus 1.641 8 for pristine SC-NM91, demonstrating that optimized Mg/Nb/Ti co-doping effectively mitigates cationic disordering and stabilizes the layered structure. The SEM images indicate that SC-NM91 comprises irregular particles (the diameter of ~1 µm) with a non-uniform distribution and a broad size range, including oversized particulates. Increasing Mg/Nb/Ti doping concentration yields a significant morphological evolution. The particle distribution becomes more homogeneous, particle size gradually decreases, and the EDS mapping confirms spatially uniform elemental dispersion, verifying an effective dopant incorporation. The XPS analysis reveals that Mg/Nb/Ti doping effectively modulates the material surface electronic structure and valence state distribution, enhances structural stability, increases the Ni³⁺ proportion, consequently improving the electrochemical performance.

SC-NM91-0.5Mg@0.25Nb@1Ti has a superior rate capability across multiple current densities, significantly outperforming other specimens. This indicates that optimal doping enhances a structural stability, while maintaining high lithium-ion transport kinetics. When cycled at 1 C under different cut-off voltages (i.e., 4.3 V and 4.4 V), SC-NM91-0.5Mg@0.25Nb@1Ti electrode exhibits the maximum capacity retention rate, showing a remarkable improvement over counterparts. These results verify that multi-element doping combined with surface modification effectively enhances electrochemical properties. Furthermore, its differential capacity curves exhibit more symmetric phase transition peaks, significantly reduced voltage hysteresis, and compact/stable peak profiles, indicating enhanced phase transition reversibility and substantially improved structural stability. The electrochemical impedance spectroscopy (EIS) primarily reveal two key parameters, i.e., series resistance (R_s) and charge transfer resistance (R_ct), reflecting intrinsic material resistance and the electron transfer barrier at the electrode-electrolyte interface, respectively. After 100 cycles, SC-NM91-0.5Mg@0.25Nb@1Ti exhibits significantly lower resistance values rather than pristine SC-NM91. This demonstrates that Mg/Nb/Ti co-modification effectively mitigates electrolyte corrosion, stabilizes the interfacial structure, and facilitates the formation of arobust cathode electrolyte interphase film. Consequently, the modified electrode maintains efficient charge transfer kinetics during prolonged cycling, while retarding R_ct degradation. Finally, the cyclic voltammetry (CV) analysis reveals that the modified sample has a distinct hysteretic shift in the oxidation peak and reduces peak intensities, compared to the unmodified sample. Nevertheless, the high degree of peak overlap across cycles indicates that the synergistic doping-coating modification significantly suppresses electrochemical polarization and enhances interfacial reaction kinetics, thereby contributing to superior electrochemical performance.

This study systematically explored a synergistic co-modification strategy combining Mg/Nb bulk doping and Ti surface coating for SC-NM91 high-nickel cathodes. The optimally designed SC-NM91-0.5Mg@0.25Nb@1Ti sample that was fabricated via high-temperature solid-state synthesis could exhibit the superior structural stability and electrochemical performance. It demonstrated a capacity retention of 89.2% at 4.3 V after 100 cycles, significantly exceeding the unmodified counterpart (i.e., 73.3%), while maintaining a retention of 66.5% at 4.4 V, indicating the exceptional high-voltage stability. The mechanistic investigations revealed that Mg doping primarily suppressed Li/Ni cation mixing and inhibited the H1→M phase transition at low voltages, while Nb doping stabilized oxygen frameworks, mitigated oxygen release under high-voltage conditions, and enhanced H2→H3 phase transition reversibility. Ti⁴⁺doping reinforced transition metal layer stability and suppressed Ni⁴⁺-induced lattice oxygen release at high voltages, extending cycle life. The concomitant formation of TiO₂/LiTi₂O₄ coating layers during thermal processing effectively blocked parasitic reactions and boosted electronic conductivity, collectively improving interfacial integrity and rate capability. The electrochemical characterization confirmed reduced R_ct post-cycling and diminished redox peak potential separation in CV, evidencing enhanced reaction kinetics and suppressed polarization. This co-modification approach could elevate the comprehensive performance of SC-NM91 cathodes, establishing an effective paradigm for developing high-energy-density lithium-ion battery cathodes with a robust stability.

Diamond is a novel optoelectronic material with a tremendous application potential, injecting new vitality and opportunities into the development of optoelectronic technology. In laser technology, diamond exhibits excellent gain parameters, stability, and thermal properties, offering outstanding advantages in high-power laser applications. The existing applications in high-power Raman and Brillouin lasers yield remarkable results. Doped diamond serves as a probe material with superior performance parameters and high irradiation resistance, enabling stable high-precision detection and extending detector lifespans in harsh environments. In the UV and deep UV wavelength bands, diamond outperforms predecessor materials (e.g. silicon) in terms of stability and durability.

Diamond has attracted recent attention in the semiconductor field during the post-Moore era, demonstrating an exceptional application potential in electronic devices. Research on diamond Schottky barrier diode (SBD) and diamond p-n junction diode becomes popular, with a significant progress achieved in breakdown voltage, switching time, on-resistance, and other performance parameters.

Therefore, the following outlooks are described for the utilization of optoelectronic properties of diamond. 1) The material quality is crucial for its optoelectronic applications. However, the synthesis technology for high-quality, low-defect diamond remains immature. Future research must focus on reducing the synthesis costs of optical-grade and electronic-grade diamond with an enhanced growth rate. 2) Despite diamond possesses excellent thermal properties, thermal lensing effects still occur during high-power laser operation. The in-depth studies of heat sources and heat distribution within crystals are necessary to achieve higher power and conversion efficiency in diamond lasers. 3) Elemental doping is a critical challenge for diamond-based devices, especially difficult for n-type doping. Future research should conduct further mechanistic and experimental studies on n-type doping of diamond. 4) Most diamond electronic devices are still in the research stage, with considerable progress needed before large-scale, practical applications can be realized, urgently requiring more extensive theoretical and experimental efforts.

The poor interface characteristics between inorganic perovskite and the electron transport layer limit the improvement of the photovoltaic performance of inorganic perovskite solar cells (IPSCs). In this paper, the buried interface was treated with ethylenediaminetetraacetic acid (EDTA), and four carboxyl groups of EDTA reacted with the hydroxyl groups of SnO₂ to improve the interface characteristics, enhance the crystallization quality of the inorganic perovskite film, reduce the defect state density and suppress non-radiative recombination. Finally, the n-i-p type device with the composition of CsPbI_2.25Br_0.75 prepared in air achieved a power conversion efficiency (PCE) of 18.84% and excellent stability.

The In-doped Tin Oxide (ITO) glass substrate was ultrasonically cleaned in glass cleaner, deionized water and isopropyl alcohol solution for 20 min, respectively. Before the use, the FTO substrate was treated with ultraviolet ozone for 20 min. Then, 12% SnO₂ nanosolution was diluted for three times with water and spin-coated on the surface of ozone-treated ITO glass at 3000 r/min for 30 s, followed by annealing in air at 150 ℃ for 30 min. After cooling to room temperature, 0.1 mg/mL EDTA (H₂O) was spin-coated on the surface of SnO₂ and annealed at 100 ℃ for 10 min. The preparation of perovskite precursor solution and thin film was consistent with the that from previously reported literature^[30], except that the preparation environment of the perovskite film was changed in air with a humidity of < 25%. 40 μL of Spiro-OMeTAD was spin-coated on the surface of perovskite film at 3000 r/min for 30 s as a hole transport layer. Finally, 80 nm of Au was evaporated on the surface of the hole transport layer by evaporation equipment as a metal electrode.

The pinholes on the surface of the perovskite in the Target group are significantly reduced, corresponding to a lower defect state density and a superior photovoltaic performance. The PL intensity of the Target group films is significantly greater than that of the Control group, indicating that non-radiative recombination is suppressed after EDTA treatment. After EDTA treatment, the average carrier lifetime increases from 75.10 ns to 113.31 ns. The optimum PCE is increased from 16.68% of the control device to 18.84%. The current density is verified by the external quantum efficiency test of the solar cell. The integral current density increases from 18.42 mA/cm² to 18.78 mA/cm² due to the improvement of the interface contact characteristics between SnO₂ and perovskite by EDTA. The steady-state output power curve of the best PCE device of the target device is negligible within 280 s. Two types of devices are placed in an environment at 25 ℃ and a humidity of 20%-30%. After 250 h, the control device retains 73.39% of its initial PCE, while the Target device maintains 81.41%. The improvement in stability is attributed to the EDTA enhancement of the interface contact between SnO₂ and the inorganic perovskite, suppressing non-radiative recombination at the interface and reducing the defect state density.

The EDTA was used to modify the buried interface. The four carboxyl groups of EDTA reacted with the hydroxyl groups of the SnO₂ layer, improving the interface contact characteristics between SnO₂ and perovskite and facilitating the efficient extraction of electrons. Non-radiative recombination at the interface was suppressed and the defect state density was reduced. Ultimately, a n-i-p type device with a composition of CsPbI_2.25Br_0.75 prepared in air achieved a PCE of 18.84%. This could provide a scientific approach for advancing the practical application of IPSCs.