In the lightweight industry, Al–Cu–Mg alloys can be used as an alternative to steel materials and are expected to be widely used in automotive transportation and military equipment. However, hot tearing defects tend to occur easily during the casting process, posing a major challenge to its defect-free casting. In this paper, the effect of cooling rate on microstructure and hot tearing sensitivity of the alloy was studied by using a “cross” hot tearing mold from the perspective of variable cross-section size and mold temperature. The results indicated that with the decrease in cooling rate, the columnar grains of the alloy tended to grow, the dendritic arm spacing increased, and the microstructure of the alloy was coarsened. The cracking susceptibility coefficient (CSC) value of the alloy decreased from 0.675 to 0.476, and the hot tearing susceptibility (HTS1) value reduced from 220 to 12. Therefore, reducing the cooling rate was beneficial to reduce the hot tearing tendency of the alloy. The HTI value and equivalent stress calculated by a commercial simulation software were consistent with the variation law of the HTS1 value and CSC value measured by experiments. The appropriate reduction of the cooling rate promoted the feeding of the residual liquid phase to the hot tearing and prolonged the time of the alloy to release the stress so that the alloy had enough time to relieve the stress through the slip between the grains, thereby reducing the hot tearing tendency of the alloy.

This study in-situ fabricates (TiB + Ti5Si3)/TC4 composites with a dual quasi-continuous network structure through casting. The work systematically investigates the effects of the reinforced phase content on microstructure, mechanical properties, and tribological performance. Results show that Ti5Si3 particles significantly alter the microstructure. TiB whiskers transform from long acicular to short acicular morphology. Ti5Si3 particles precipitate at alpha/beta phase interfaces and inside beta phases. This precipitation behavior forms the dual quasicontinuous network structure. With increasing reinforced phase content, the mechanical properties and tribological performance undergo initial enhancement followed by degradation. The (3 vol% TiB+4 vol% Ti5Si3)/TC4 composite (S-3) demonstrates optimal comprehensive properties. Its hardness reaches 59.33 HRC, compressive strength hits 1875 MPa, and plasticity reaches 20.4 %. This composite also shows notable wear resistance. The strengthening mechanism involves matrix grain refinement, solid-solution strengthening, load transfer, thermal mismatch strengthening, and Orowan strengthening induced by reinforced phases. In addition, the reinforced phases hinder crack propagation, which enhances the composites' plastic deformation capacity and wear resistance. This work proves that optimizing the TiB/Ti5Si3 ratio enables improvement of the properties of titanium matrix composites. It provides a theoretical basis for designing composites with high strength, high plasticity, and favorable wear resistance.

The problem of insufficient oxidation resistance of a TiAl alloy above 800 degrees C has limited its broader application. In this paper, Ni/Al composite coatings were deposited on TiAl alloy. The high-temperature oxidation resistance and thermal shock behavior of the Ni/Al coatings were systematically investigated. The composition of the oxidized coating from the surface to the interior consisted of an Al2O3 oxide film, a NiAl compound layer, a Ni layer, a TiAl3 diffusion layer, and a Ti2Al diffusion layer. The Al2O3 oxide film and NiAl compound layer effectively hindered the inward diffusion of oxygen and the outward diffusion of titanium. The local failure of the coating in thermal shock experiments began with the initiation and propagation of pores and cracks.

Soft magnetic composites (SMCs) are essential for next-generation power devices owing to their superior high-frequency performance and low losses. However, the the incorporation of conventional non-magnetic insulating media during the coating process generates the demagnetizing field and causes magnetic dilution effects, posing a significant challenge for achieving simultaneous high permeability and low loss in SMCs. Here, we propose a strategy for optimizing electromagnetic properties through superparamagnetic nanoparticle-mediated interfacial enhancement, and successfully fabricated FeSi/CoFe2O4 SMCs. CoFe2O4 nanoparticles with high electrical resistivity and superparamagnetic characteristics (coercivity approximate to 0) uniformly dispersed on FeSi powder surfaces block eddy currents via insulating interfaces while stabilizing domain wall motion, thereby achieving a concurrent reduction in both eddy-current and hysteresis losses. Interfacial exchange coupling between the CoFe2O4 and FeSi matrix promotes magnetic moment rotation and reduces pinning, enhancing permeability and mitigating magnetic dilution. The fabricated FeSi/CoFe2O4 SMC exhibits an ultralow loss of 429 mW/cm3 (100mT/50 kHz) and a high permeability of 65. These findings offer a new pathway to balance magnetic dilution and power loss, which provides a useful guidance for the development of high frequency electromagnetic devices.

Al-Ti alloys draw significant attention owing to the Al3Ti phase's low density, high melting point, thermal stability, and high Young's modulus. However, the coarse structure and uneven element distribution in cast binary Al-Ti alloys reduce their strength, limiting industrial applications. This issue can be mitigated by alloying and increasing the cooling rate. This study prepared Al-3Ti-xV (x = 1,2,3) alloys via melting casting, investigating the effects of V content and cooling rate on solidification characteristics, microstructure, and tensile properties. Results indicate that increasing V content forms a (Ti,V) solid solution with higher melting point and stability during solidification, raising the alloy's characteristic temperature except for a reduced solidification temperature range of α-Al. The alloy's microstructure comprises α-Al, Al3(Ti,V), and Al45V7 phases. The α-Al diffraction peak slightly shifts due to lattice mismatch from V solid solution, while the Al3(Ti,V) phase's lattice parameter decreases, enhancing structural stability. With increased V content, the Al3(Ti,V) phase transforms from needle-like to block-like and finally rod-like. Both elevated cooling rates and higher V content effectively refine grain size and Al3(Ti,V) phase dimensions, promoting uniform distribution. Simultaneously, the proportion of Al3(Ti,V) phase decreases. Tensile properties improve with higher cooling rates and V content, attributed to three main factors: the higher bulk, shear, and Young's moduli of the Al3(Ti,V) phase post-V solid solution; the maximum growth limiting factor Q value reached with excessive V addition, significantly reducing grain size and enhancing strength through heterogeneous nucleation forming Al45V7 phase. Water cooling enhances alloy strength by inhibiting Al3(Ti,V) phase precipitation, forming supersaturated solid solutions, increasing nucleation density, refining grains, creating compositional supercooling zones, and homogenizing alloy composition. Under water cooling, Al-3Ti-3 V exhibits a tensile strength of 159.02 MPa.

This work aims to investigate temperature-load coupling effects on high-temperature tribological behaviors of (TiBw+Ti5Si3)/TC4 composites. It intends to overcome the insufficient high-temperature wear resistance of titanium alloys and supplement research deficiencies of TMC wear mechanisms under complex service conditions. Dry sliding tests were performed on a pin-on-disc tribometer at 100–600 ℃ and 300–600 N (600℃). The results show that the composite has a critical temperature of 300 ℃ and a critical load of 500 N. Below these thresholds, the tribo-layer is loose and discontinuous, dominated by abrasive and adhesive wear with severe plastic deformation and stress concentration in the subsurface. Above the thresholds, a compact tribo-layer consisting of TiO2, FeO, Fe2O3 and reinforcements forms, leading to a transition to mild oxidative wear. Compared with TC4 alloy, the TMCs showed a 78% reduction in wear rate under the same tested conditions. The minimum specific wear rate reaches -1.55×10-7 mm3/(N·mm) at 600 ℃/500 N. TiBw improves wear resistance via load transfer and grain pinning and acts as a skeleton to stabilize the tribo-layer, which provides physical isolation and lubrication for friction reduction. In the high-wear state, the subsurface deformation zone is characterized by extensive plastic deformation and stress concentration. In the low-wear state, the stress distribution becomes uniform and the deformation zone shrinks. The wear mechanism transitions from mechanically dominated wear to oxidative wear. The composite exhibits optimal performance at ≥300 ℃ and about 40 MPa contact stress, providing theoretical support for hot-end components in aerospace engines.

NiTi alloys are investigated as the fourth-generation aviation bearing materials due to their excellent high-temperature resistance, wear resistance, and corrosion resistance. However, their elastic modulus and hardness still need to be further improved. Therefore, in this study, Hf was added to the NiTi alloy by microalloying to further improve its mechanical properties and wear resistance. Research shows that the NiTiHf alloy was based on a B2-NiTi matrix, and with the addition of Hf, the amount of the Ni₃Ti₂ phase formed increases. When the Hf content exceeded 12wt.%, abundant lath-shaped Ni₃Ti softening phases were formed. With increasing Hf addition, the nanoindentation hardness and ultimate compressive strength of the alloys exhibited a trend of first increasing and then decreasing. Among them, the 56Ni36Ti8Hf alloy possessed the optimal comprehensive mechanical properties, with a nanoindentation hardness of 5.77GPa and an ultimate compressive strength of 2481MPa. At room temperature and 600℃, the specific wear rate of the 56Ni36Ti8Hf alloy increased, while its friction coefficient decreased as the wear load increased (100N-300N). The Hf improved the deformation resistance of the matrix, thereby enhancing the wear resistance. Furthermore, the Ni3Ti2 strengthening phase could inhibit the local high concentration of dislocations and reduce the contact between abrasive particles and the matrix, preventing matrix instability and cracking. The main wear mechanisms were abrasive wear, adhesive wear, and oxidative wear. This study shows that moderate Hf addition can enhance the mechanical properties and wear resistance of NiTi alloys, providing a new approach for their further application in aviation bearing materials.

The high temperature tensile experiment of Ti-47.5Al-2.5V-1.0Cr-0.2Zr alloy was completed at 750-900 degrees C and strain rate of 10-5-10-3 s-1. The processing map corresponding to the tensile process was established, and both optimal and instability zones were identified. The microstructure of different zones of processing map were observed in detail, and the justness of processing map was proved. The results show that the strain rate sensitivity index and energy dissipation rate increase with change of deformation conditions from low temperature/high stretching rate to high temperature/low stretching rate. The parameters of thermal tensile instability zone are: 750-795 degrees C/10-4-4 x 10-4s-1 and 750-778 degrees C/10-4-10-5s-1. The optimal hot deformation parameters are as follows: the temperature is 880-900 degrees C and the strain rate is 2.5 x 10-4-10-5s-1. The obvious cracks and holes appear in the deformation structure corresponding to the instability zone, which are preferentially generated at the lamellar interface. The ratio of recrystallized structure corresponding to the optimal deformation parameter zone is higher than that in the instability zone, and the plastic deformation ability is greatly improved. The deformation characteristics of the instability zone are the dislocation pile-up, which is caused by the hindrance of the lamellar boundary and lamellar structure to the dislocation movement, and the substructure formed by the entanglement of the high-density dislocation regions in the lamellar structure. At the same time, there are also twins with a certain angle between the lamellar structure. The characteristics of deformation structure corresponding to the optimal deformation parameter region are dislocation, twin and recrystallization. The dislocation density in the recrystallized structure decreases, which can slow down the stress concentration inside the deformed structure, and the probability of instability such as cracks inside the alloy decreases.

Strength and plasticity are essential properties of Al-Cu alloys for the development of high-end equipment. However, the composition design range of Al-Cu alloys is broad, which leads to a trade-off between strength and plasticity. Consequently, achieving simultaneous enhancement of both strength and plasticity presents a greater challenge. To improve the traditional "trial-and-error" material design approach, this study integrates two interpretable machine learning models into a unified system: one model for predicting ultimate tensile strength (UTS) and another for predicting elongation at break (EL). The method performs multi-objective optimization and, in doing so, identifies the element properties that influence the UTS and EL of Al-Cu alloys. Elements with higher solid solubility, electrical resistivity, and enthalpy of vaporization, as well as lower lattice constant and nearest neighbor distance in the Al matrix, enhance the UTS of Al-Cu alloys. Furthermore, alloying elements with lower density and larger covalent radii improve the EL of Al-Cu alloys. Based on the interpretability analysis, Ni and Er are selected as alloying elements due to their significant synergistic effects in improving both strength and plasticity. The Al-6.7Cu-0.8Ni-0.16Er (wt.%) alloy is heat-treated appropriately, resulting in a UTS of 421.16 +/- 5 MPa and an EL of 13.2 +/- 0.4 %. Microstructural characterization reveals a uniform grain size distribution in the samples. The high volume fraction of nanoscale precipitates, which include 0 ''/0 ' phases and Al3Er phases, is uniformly distributed within the matrix, thereby contributing to the synergistic enhancement of both strength and plasticity.

The automotive industry increasingly relies on numerical simulations to predict the geometry and forming processes of complex curved parts. Accurate yield stress functions that cover a wide range of stress states, such as uniaxial tension, equi-biaxial tension, near-plane strain tension, and simple shear, are essential for implementing virtual manufacturing technologies. In this work, a new additive-coupled analytical yield stress function, CPN2025, is proposed to accurately describe plastic anisotropy under various loading conditions. CPN2025 integrates the Poly4 anisotropic yield criterion with the Hosford isotropic yield criterion under a non-associated flow rule. A non-fixed-exponent calibration strategy is introduced, overcoming the limitations of existing yield criteria that typically offer curvature adjustment with only positive or negative correlations. CPN2025 is compared with other non-associated yield functions, including SY2009, CQN2017, and NAFR-Poly4, to evaluate its performance in predicting the plastic anisotropy of DP490, QP1180, AA5754-O, and AA6016-T4. Results show that, while meeting convexity requirements, the additive-coupled approach not only provides greater flexibility than the multiplicative-coupled but also simplifies the acquisition of partial derivative information. CPN2025 delivers the highest accuracy in characterizing anisotropic yield behavior, particularly for near-plane strain tension and simple shear loadings. Additionally, incorporating more uniaxial tensile yield stress-calibrated material parameters significantly improves the prediction capacity of in-plane anisotropic behavior. The use of anisotropic hardening concepts enhances the model's capability to capture the subsequent yield behavior across the entire plastic strain range. (c) 2025 Published by Elsevier Ltd on behalf of The editorial office of Journal of Materials Science & Technology. This is an open access article under the CC BY license (http://creativecommons.org/licenses/by/4.0/)

To improve oxidation resistance, an Al/ NiAl composite coating was prepared on a TiAl alloy via arc spraying. The microstructure, composition, element distribution, and thermal cycling resistance of the coating before and after oxidation were studied. The oxidation kinetic behavior and failure mechanism were systematically studied. The prepared coating had a dense and uniform structure and good bonding with the substrate. The oxidation weight gain curves showed initial rapid weight gain followed by stable weight gain. The oxidation weight gain of the samples with the Al/NiAl coating was significantly lower than the uncoated substrate. The oxidation rate constant increased as the temperature increased. Oxidation at 800 and 850 degrees C for 20 h led to the formation of a diffusion layer mainly composed of the NiAl3, Ni2Al3, and NiAl phases. Oxidation at 900 degrees C for 20 h led to the formation of a diffusion layer mainly composed of the Ni2Al3 and NiAl phases. After oxidation at 800 or 850 degrees C for 100 h, the coating structure showed no cracks or spalling, and there was no obvious O invasion inside the coating. When oxidized at 900 degrees C for 100 h, there were micropores and cracks in the coating, but O had not invaded the substrate. The local failure of Al/NiAl coating after thermal cycling began with crack initiation and propagation in the edge region. Overall, the Al/NiAl composite coating significantly improves oxidation resistance via a synergistic effect of in situ NiAl intermetallic compounds and an Al2O3 film.

To solve the problem of low plasticity in homogeneous particle-reinforced composites,micro-nano dual-scale near-network (TiC + Ti5Si3)/TC4 composites were prepared by in-situ melting-casting technology. The microstructural evolution, strengthening and friction mechanisms of micro-nanoscale composites were systematically investigated. The results showed that with the increase of the reinforced phase content, the morphology of micron-sized TiC changes significantly from the initial short plume to granular gradually, and the nano-sized Ti5Si3 particles change from small particles to ellipsoidal gradually precipitated at the beta-Ti and alpha/beta interfaces. The (3 vol%TiC+3 vol%Ti5Si3)/TC4 composites (TMCs-2) exhibits excellent mechanical properties with compressive strength of 1774 MPa, plasticity of 24.5 % and hardness of 52.8 HRC. The increase in strength of the composites is attributed to the synergistic effect of matrix (fine grain strengthening, solid solution strengthening) and particle strengthening. The special structural design can effectively hinder the propagation of cracks, lead to crack deflection and passivation, and delay the fracture of composites. The addition of TiC and Ti5Si3 reinforced phases can improve the shear resistance of the surface and subsurface layers of the composites, which can inhibit the emergence of microcracks during sliding wear process, and the wear resistance is significantly improved. At the same time, the micro-nano structure design effectively avoided stress localization and significantly improved the deformation coordination ability of the composites.

The Fe-containing intermetallic compounds (FIMC) induced by Fe impurities in Al-Si alloy system and the regulation of solidification structure are the key challenges to improve the properties of the alloy. In this study, the microstructure evolution and phase transformation mechanism of Al-6Si-xTi-1Fe alloy are systematically revealed by synergistic regulation of Ti content (1-3 wt%) and cooling rate (air-cooled / water-cooled). Microstructural analysis reveals that the alloy predominantly comprises an alpha-Al matrix with dispersed eutectic Si, Al3Ti, and theta-Al13Fe4/alpha-Al8Fe2Si/beta-Al5FeSi phases. Notably, exceeding 2 wt% Ti content induces growth in alpha-Al grains through Al3Ti phase activation. Quantitatively, low-angle grain boundaries exhibit an increase from 25.23 % to 39.37 %, while average grain dimensions expand from 113.3 mu m +/- 4.2 (Al-6Si-1Ti-1Fe, wt%) to 132.8 +/- 5.1 mu m (Al-6Si-3Ti-1Fe, wt%). The grain size of the water-cooled alloy is 30-40 % lower than that of the air-cooled alloy, and more than 42 % of the primary theta-Al13Fe4 phase is retained by inhibiting element diffusion. Mechanical tests indicate that increasing Ti content and cooling rate enhance tensile strength (e.g., 18.6 % increase in AS-3Ti compared to AS-1Ti) but reduce ductility. Combined with TEM and EBSD analysis, the diffusion control mechanism of the Fe-Si phase transition path (theta-Al13Fe4 ->alpha-Al8Fe2Si ->beta-Al5FeSi) in Al-6Si-xTi-1Fe alloy is clarified. This investigation establishes a theoretical basis for optimizing the titanium addition strategy and cooling process of Al-Si-Ti-Fe alloy. The findings deliver actionable insights for engineering enhanced cast aluminum alloys with superior performance characteristics.

The characteristics of energy and microstructure 54Ni46Ti alloy are studied by hot compression simulation test, XRD, EBSD, and TEM observation. The unstable interval and the optimum processing parameters are accurately predicted by constructing the hot processing map. In this study, the energy analysis of the hot deformation process was realized by combining the power dissipation rate and the microstructure characteristics. As a result, the 54Ni46Ti alloy has a low-temperature unstable region, a high-temperature unstable region, and a suitable processing region under the experimental parameters. In the unstable region, the unstable crack appears due to the high dislocation density inside the alloy structure. The average dislocation density of the alloy in unstable different areas is 4.633 x 1014 m-2 and 2.879 x 1014 m-2, and the dynamic recrystallization (DRX) content is 3.9 % and 48.1 %, respectively. In the suitable processing region, the eta value is higher. Under the conditions of 850 degrees C and 0.01 s-1, the DRX fraction of the alloy is 50.4 %, and the average dislocation density is 1.397 x 1014 m-2. At 900 degrees C, 0.01 s-1, the DRX fraction is 59.6 %, and the average dislocation density is 0.841 x 1014 m-2. In the suitable processing region, the softening mechanism is DRX.

Breaking the strength-plasticity inversion dilemma of titanium matrix composites in engineering materials research is still a challenging hot task. In this work, we have demonstrated a simple heat treatment method to achieve a micro-nano-scale quasi-continuous network structure with micron-sized TiC particles and nano-sized Ti5Si3 particles in (3 vol% TiC+3 vol% Ti5Si3)/TC4 composites. Through quenching treatment, we successfully achieved the re-dissolution of Ti5Si3 particles and the formation of quenched matrix structure (including lamellar martensite (alpha'-Ti) and residual beta-Ti). TiC particles are distributed in a network at the grain boundary, which further limits the excessive growth of the matrix. Subsequently, we applied aging treatment to activate different growth mechanisms of the matrix and different precipitation characteristics of Ti5Si3 particles to form finely dispersed regions of different arrangement modes of Ti5Si3 precipitation particles in the beta matrix. For the 800 degrees C aged composites, the compressive strength reached 1850 MPa and the compressive strain reached 26.79 %. The excellent ductility of the composites is attributed to its unique microstructure design. This micronano dual-scale design prevents strain localization and allows dislocations to be fully activated in the alpha phase and ductile beta region. Meanwhile, the high strength of the composites can be attributed to the enhanced back stress effect caused by the strain distribution of the micro-nano scale near-network structure design. Our research shows a simple and effective method, which provides a new insight into breaking the strength-plasticity inversion dilemma of metal matrix composites.

In this paper, the solidification characteristics of Al-Ti alloys and the precipitation behavior of Al3Ti phases at different Ti contents and cooling rates were investigated by cooling curve thermal analysis. By heating the Al-xTi (x = 1, 2, 3) alloys melt to 1100 °C and cooling it under near-equilibrium solidification and non-equilibrium solidification conditions, the precipitation growth characteristics of the Al3Ti phase were analyzed under each solidification condition. The results demonstrated that the precipitation temperatures of the Al3Ti phase in Al-xTi (x = 1, 2, 3) alloys increased from 774.65 to 920.26 °C with the increase in Ti content from 1 to 3 wt.

Nanoindentation test, high-temperature compression test, SEM, EBSD, and TEM observations are performed to investigate the effects of Hf additions on the microstructure and properties of NiTi alloy. The high-temperature deformation behavior of NiTi-8/12Hf alloys is discussed. The constitutive model and hot processing map are constructed, and the optimal processing interval of the two alloys is predicted. The results show that the content and size of precipitates increase with the addition of Hf. The nanoindentation hardness of the matrix with different Hf content increased from 3.36 +/- 0.11 GPa to 5.47 +/- 0.13 GPa. The main strengthening mechanism of the addition of the Hf to improve the strength is the solid solution strengthening effect and the load transfer effect. With the addition of 8 wt% and 12 wt% Hf, the instability areas are expanded. The optimal processing area of 8/12Hf alloys are 900 degrees C, 0.01s(-1). Under this condition, the microstructure of the alloy has a high DRX volume fraction and low average rho GND. As hot deformation progresses, the accumulated energy inside the alloy increases, leading to the activation of dislocations and the formation of more DDRX at grain boundaries. Dislocations within the grains aggregate to form LAGBs. The softening mechanism of 56Ni-Ti-8/12Hf alloy are DDRX and dynamic recover.

The high temperature tensile test of Ti-47.5Al-2.5 V-1.0Cr-0.2Zr alloy was carried out by electronic universal testing machine under the condition of 750-900 degrees C/10- 5-10- 3 s- 1. The hot tensile stress-strain curves were analyzed, and the constitutive model under hot tensile conditions was established. The microstructure transformation rule and deformation mechanism during tensile process were determined. The results show that the hot tensile curve is longer in the steady-state flow stage corresponding to lower strain rate and higher tensile temperature, the true stress declines and the elongation at break increases. The constitutive equation was established based on the tensile curve data, and the corresponding thermal activation energy was 310.3 kJ/mol. As the rise of tensile temperature and the decline of strain rate, the proportion about cross-layer fracture in the tensile fracture morphology decreases, the number of dimples increases, more lamellar structures change into recrystallized structures, and the softening effect of the alloy is more obvious. The dislocation deformation mechanism mainly includes the existence of dislocation slip and climb, dislocation intersection and dislocation ring or dislocation network formation. Twinning deformation is also another important mechanism of high temperature tensile deformation of TiAl alloy. Twins are formed in parallel with each other, so that the deformation can be further carried out. The dislocations and twins in the deformed microstructure will provide nucleation conditions for recrystallized grains. The dynamic recrystallization(DRX) grains are preferentially formed around the grain boundary and the vicinity of dislocation and twin is also preferred nucleation site for DRX. The DRX behavior is the main softening mechanism, and DRX size and volume fraction corresponding to lower tensile rate and higher tensile temperature are larger.

Developing efficient, stable and low-cost electrocatalysts is a viable approach to solve the current energy crisis. It is found that increasing the surface area of the electrodes can effectively promote the electrocatalytic efficiency. Herein, the atmospheric plasma spraying (APS) technology was used to prepare FeCoNi-Ni3C alloy coating by adding Ni3C powder to FeCoNi powder with an equal molar ratio. After mechanical mixing, the atomic ratios of Ni3C in the powder are 25 %, 50 %, and 75 %, respectively. The results prove that the pores on the surface of the coating have increased after Ni3C doping, which can provide more active sites in the electrocatalytic process to promote the electrocatalytic reaction. By controlling the proportion of Ni3C, the porosity of the coating surface can be effectively regulated. The results suggested that in 1.0 M KOH electrolyte and 10 mA cm-2, the FeCoNi coating shows an overpotential of 191 and 277 mV for HER and OER, respectively, the HER overpotential of 50 at % Ni3C FeCoNi-Ni3C coating is 105 mV, and the OER overpotential is 212 mV. It is worth noting that the 50 at % Ni3C FeCoNi-Ni3C coating has a low Tafel slope of 45.78 mV dec-1 (HER) and 44 mV dec-1 (OER). Meanwhile, the attenuation of the overpotential of the 50 at % Ni3C FeCoNi-Ni3C coating after the stability test is almost negligible, indicating that the prepared catalyst has excellent electrocatalytic stability. Furthermore, the 50 at.% Ni3C FeCoNi-Ni3C coating catalyst has a low potential of 1.664 V at 10 mA cm-2 in a water-splitting system. This work provids a new idea for designing inexpensive electrocatalysts.

The corrosion process of Q345 steel in simulated industrial atmospheric surroundings using NaHSO3 as the corrosion medium was performed. Corrosion weight loss, X-ray diffraction (XRD), electron probe microanalysis (EPMA), laser scanning confocal microscopy (LSCM), and scanning electron microscopy (SEM) were utilized to investigate the corrosion behavior of Q345 steel samples at various corrosion times. The results indicate that, in the industrial atmospheric acceleration system, the corrosion law of Q345 steel follows an exponential function model and that as the corrosion period lengthens, the rate of corrosion declines steadily. gamma-FeOOH, alpha-FeOOH, Fe3O4, Fe3O2, and FeO make up the majority of the corrosion products on the surface of rust layer, and the rust layer structure is generally loose in the first stages of corrosion. As the corrosion time lengthens, the corrosion products transform from needle-like to cluster-like and the rust layer will become thicker. In addition, there is a segregation of the elements Cr, S, and O in the rust layer of Q345 steel.