With the rapid development of industry，agriculture，mining and urbanization，a large number of heavy metals and other pollutants enter the soil environmental system，and the combined pollution of heavy metals in soil caused by this problem has attracted much attention. According to the 2014 National Soil Pollution Status Report，19.4% of China's arable land has exceeded the standard for heavy metal pollutants such as Pb，Cd and As，with the sites exceeding the standard for these three typical heavy metals ranking at the top，resulting in a polluted area of over 50 million acres. Soil heavy metal pollution is characterized by long-term persistence，durability，and difficulty in degradation. Through surface and subsurface runoff，it can be transferred from the soil to surrounding water bodies，exacerbating water heavy metal pollution. At the same time，heavy metals in land and water can be absorbed by crops，entering the food chain and accumulating in organisms，causing significant harm to human health. Pb has irreversible effects on the nervous system and children's intellectual development. Cd is a highly toxic heavy metal，long-term exposure to cadmium-contaminated environments may lead to diseases such as kidney damage，osteoporosis，and cancer. As is associated with health issues including cancer，skin diseases，and cardiovascular diseases. However，the coexistence of heavy metals such as Pb，Cd and As in soil in composite pollution poses greater environmental hazards compared to single pollution. Therefore，it is of great significance to comprehensively understand the current situation，characteristics，and remediation technologies of heavy metal composite pollution for the prevention and control of heavy metal pollution and the safe utilization of soil. This review provides a comprehensive overview of the current status，sources of pollution，and distribution and migration characteristics of Pb，Cd and As in soils affected by composite pollution. It particularly emphasized the impact of soil pH，redox potential （E_h），soil organic matter （SOM） and soil types on the migration and transformation of Pb，Cd and As. The study presented a summary of the research progress in the remediation of Pb，Cd and As composite pollution using physical remediation methods，solidification/stabilization techniques，and bioremediation approaches. It discussed the advantages，disadvantages，and applicability of various soil remediation technologies and provides an outlook on future development directions. Specifically，the ex-situ soil washing method had a fast remediation rate but was expensive，easily disrupts soil structure，and might cause secondary pollution. The electrokinetic remediation method had simple equipment operation but was relatively costly，consumed a significant amount of energy，and might pose safety hazards. The bioremediation method could improve soil quality and maintain ecological balance but had a slow remediation process and is highly influenced by the environment. The solidification/stabilization techniques had become the mainstream technology for the remediation of composite pollution in soils due to their high efficiency，low cost，and easy implementation. Furthermore，due to the pressing demand for the large-scale disposal of metal mine wastes in China，the research on developing new solidification/stabilization materials utilizing local mining solid wastes for the remediation of Pb，Cd and As composite polluted soils would become a key focus in the field of solidification/stabilization technologies.

In harsh marine environments，traditional diamond-like carbon（DLC）films as protective coatings have problems of wear and corrosion failure，which seriously affect the reliability and service life of marine engineering equipment. Ti/TiN/TiCN/Ti-DLC composite films were prepared on 316L stainless steel by medium-frequency magnetron sputtering technology to improve the wear and corrosion resistance of the traditional DLC films. Scanning electron microscopy（SEM），Raman spectroscopy，X-ray photoelectron spectroscopy（XPS）and X-ray diffraction（XRD）were applied to analyze the effects of different Ti doping contents on the structure and morphology of composite films. Furthermore，the effects of different Ti element doping contents on the mechanical properties and wear and corrosion resistance of the composite films were investigated by nanoindentation test，bonding force test，friction and wear test，and electrochemical test. The results indicated that the surface of multilayer Ti-DLC films with different Ti element doping contents was dense and free of obvious defects，but there were cluster particles on the surface of the films. Compared with multilayer pure DLC films，the doping of Ti element reduced the density and size of cluster particles on the surface of the films. With the increase in Ti doping content in DLC film layer，there was an initial rise followed by a subsequent decline in sp³ carbon content within DLC film layer. With the increment of Ti target deposition current，the kinetic energy of sputtered Ti particles gradually intensified，facilitating their effective bombardment on the amorphous carbon-based network structure. Consequently，this promoted easier formation of sp³ carbon by C atoms and led to an increase in the content of sp³ carbon within the film. However，with the further increase of Ti target deposition current，Ti element content in the film gradually increased，resulting in the catalytic effect of Ti element playing a leading role in DLC film and the increase of sp² carbon content in DLC film layer. The maximum sp³ carbon content in DLC film was observed at Ti element content of 5.10%（atom fraction）. The doping of Ti element into DLC film layer could enhance the mechanical properties of the film. With the increase in Ti element doping content，the adhesive force of the film initially increased and then decreased. The adhesive force reaches its maximum value of 27.6 N when Ti content was 6.31%. However，there was little difference in the adhesive force of multilayer Ti-DLC film when Ti content in DLC film was greater than or equal to 5.10%. Moreover，as Ti element doping content increased，both the hardness and elastic modulus of the film exhibited an initial increase followed by a decrease，which was consistent with variations in sp³ carbon content within the film. This suggested that changes in the electronic structure of carbon within Ti-DLC film layer significantly influenced its nano hardness. The friction coefficient of 316L stainless steel was approximately 0.80 under a load of 2 N，while the friction coefficient of multilayer Ti-DLC films，prepared with varying contents of Ti element doping，ranged between 0.2 and 0.4. Notably，the friction coefficient of the prepared multilayer Ti-DLC films was significantly lower than that of 316L stainless steel. This observation highlighted the excellent wear resistance and friction reduction properties exhibited by the multilayer Ti-DLC film，which effectively served as a protective barrier for 316L stainless steel. According to the analysis of electrochemical impedance results，it could be concluded that when Ti element doping content was 5.10%，the corrosion resistance of multilayer Ti-DLC films was the best. This phenomenon might be attributed to changes in the surface DLC film structure caused by variations in sp³ carbon content and the size and quantity of TiC nanophase. The corrosion resistance of DLC films was closely related to sp³ carbon content within the carbon matrix. When sp³ carbon content in the film increased，the electrochemical inertia of the film surface became enhanced，leading to a decelerated electron transmission rate on the film surface and consequently resulting in higher electrochemical impedance. Meanwhile，an increase in sp³ carbon content could also contribute to a denser structure of DLC film. However，when Ti elements were doped into DLC films，TiC particles formed which created pathways for corrosive media to penetrate the film，resulting in decreased corrosion resistance. The synergistic effect between sp³ carbon content and number of TiC particles significantly impacted the structural properties of Ti-DLC films. Excessive doping with Ti led to a gradual decrease in sp³ carbon content and an increase in TiC particles，ultimately deteriorating the film's corrosion resistance. Hence，the wear and corrosion resistance of DLC films could be significantly enhanced through the combination of a multilayer structure design and Ti element doping，thereby improving the long-life service performance of DLC films in marine environments.

As a new type of energy storage device，super capacitor has the advantages of high charge and discharge power，long cycle life and large working range，and has been widely used in various industries. As the performance of super capacitors depends largely on electrode materials，exploring suitable electrode materials will become a critical step in the development of super capacitors. Among various materials，nickel cobalt oxide has received extensive attention due to its excellent electrical conductivity，high capacity，relatively friendly price and minor environmental pollution. At present，the methods for synthesis of nickel cobalt oxide mainly include hydrothermal method，sol-gel method and electrodeposition method. Among them，hydrothermal method has been commonly used due to its simple operation and relatively uniform product distribution. Surfactants are substances that can change the properties of liquids，therefore the application of surfactant in hydrothermal environments can optimize the morphology of products and improve their electrochemical performance. Here the hydrothermal method was applied to synthesize nickel cobalt oxide，which was formed on nickel foam by using cobalt nitrate and nickel nitrate as raw materials，and different types of additives including polyethylene glycol （PEG），hexadecyl trimethyl ammonium bromide （CTAB），and sodium dodecyl sulfate （SDS） were used as surfactants. The aim was to investigate the effects of surfactants on the phase，morphology and electrochemical properties of the synthesized materials. The preparation of nickel cobalt oxide mainly included pretreatment of foam nickel，synthesis of precursor and calcination of the precursor to obtain the final product. The raw material of cobalt nitrate and nickel nitrate were dissolved in deionized water and urea was added to adjust the pH value of the solution，then the surfactant was added to the above solution. After fully stirred，the solution was transferred to the hydrothermal reactor，in which the nickel foam was placed beforehand and acted as the matrix for the growth of reaction product. After that the hydrothermal reactor was sealed and heated in the oven at 120 ℃ for 6 h to obtain the precursor material. Then the precursor was washed，dried and calcined at 300 ℃ for 2 h to get nickel cobalt oxide. The sample was characterized by X-ray diffraction （XRD），X-ray photoelectron spectroscopy（XPS） and scanning electron microscopy （SEM） to determine the phase，molecular structure and atomic valence，and to observe the micro structure. The electrochemical properties of the sample were analyzed by cyclic voltammetry （CV），galvanostatic charge-discharge （GCD） and electrochemical impedance spectroscopy （EIS）. The results showed that the nickel cobalt oxide prepared without surfactant had the morphology of nanowires，but the nanowires distribute unevenly and some of them even aggregate to some extent. Compared with the sample prepared without surfactant，nickel cobalt oxide prepared with PEG （NC-PEG） had relatively slender nanowires，but the distribution of nanowires was relatively sparse； the morphology change of the sample prepared with CTAB （NC-CTAB） was not obvious； the sample prepared with SDS （NC-SDS） showed regular and dense nanowires，with the average length of the nanowires of about 500 nm，the diameter of 30 nm，meanwhile the nanowires grew in the same direction. And the nickel cobalt oxide prepared with SDS also has a larger specific surface area and pore volume. As an anionic surfactant，SDS could provide a template for the growth of nickel cobalt oxide precursor in a hydrothermal environment，ensuring uniform and regular growth of the nanowires. When nickel cobalt oxide was used as electrode material for super capacitor，the regular structure of samples prepared with SDS would conducive to sufficient contact between the electrode material and the electrolyte，therefore promoting the redox reaction and improving the electrochemical performance of the material. Through electrochemical tests，it was found that electrochemical properties of the nickel cobalt oxide samples prepared with surfactant were improved，the improvement degree depending on the type of the surfactant. The specific capacitance of nickel cobalt oxide prepared without surfactant was 356 F·g⁻¹，and the capacitance retention rate after 1000 cycles at 20 A·g⁻¹ was 80%. And dynamic analysis for this sample showed that diffusion control played a major role in the charging and discharging process. For each sample，the ability for charge storage increased with the following order：nickel cobalt oxide prepared without surfactant （NC），NC-CTAB，NC-PEG and NC-SDS，and the specific capacitance of the above samples were 352，378，564 and 1102 F·g⁻¹ respectively. Nickel cobalt oxide prepared with SDS showed bigger improvement in electrochemical performance than with PEG and CTAB. For the sample prepared with SDS，the specific capacitance increased to 1102 F·g⁻¹，the capacitance retention rate increased to 84% after 1000 cycles at a high current of 20 A·g⁻¹，and the charge transfer resistance was 0.47 Ω. The addition of SDS could improve the electrochemical performance of the prepared nickel cobalt oxide，which would provide a way for the preparation of high-performance electrode materials.

Nickel-based single crystal superalloys have become increasingly important in the manufacturing of aircraft engines and gas turbine blades due to their superior mechanical properties，including excellent high-temperature strength and superior fatigue resistance. However，these alloys suffer from the problem of high-temperature oxidation，which can significantly shorten their service life. In order to improve the oxidation resistance and prolong the service life，it is necessary to have a comprehensive understanding of their oxidation behavior. The oxidation kinetics of nickel-based single crystal superalloys can be divided into three stages：the first stage，where the oxidation follows the parabolic law controlled by diffusion；the second stage，where the oxidation rate decreases significantly due to the formation of a continuous dense alumina layer；and the third stage，where the thickness of the oxide film reaches a critical value and detachment occurs，which accelerates the oxidation rate. The oxidation kinetics of different alloys may differ due to the influence of factors such as element content and oxidation temperature. The oxidation kinetics curve exhibits a parabolic law，subparabolic law，and cubic law，and different oxidation stages show different oxidation laws due to changes in the oxide layer （whether a dense alumina layer is formed）. The oxide film of nickel-based single crystal superalloys can be divided into three layers：the outer layer of nickel oxide，the middle layer of spinel，and the inner layer of dense alumina. After a period of oxidation，γ′ phase in the matrix can be transformed into γ′ phase at the inner side of alumina film due to the depletion of Al element，forming γ′-free zone. After long-term oxidation，the thickening of the oxide film leads to the peeling of the oxide layer，leaving a large area of γ′-free zone. During the initial oxidation process，the dislocation generated by lattice mismatch can aggregate in the two phases to form a dislocation network，providing a channel for oxygen atoms to diffuse inward. Moreover，the oxidation behavior of nickel-based single crystal superalloys is affected by many factors. First，the element content of the alloy，such as Al，Cr，Si，Hf，and rare earth elements can improve its antioxidation performance of the alloy，while S，Ti，Ru，and other elements have the opposite effect. In addition，the segregation during the solidification process of the alloy can cause inconsistent oxidation behavior between dendrites and intradendritic regions. Specifically，the initial oxidation product between dendrites is mainly aluminum oxide，while the intradendritic region is mainly nickel oxide. In the long-term oxidation process，the alumina layer in the intradendritic region undergoes a process of changing from continuous dense to fragmented and dispersed，while those in the interdendritic region always remains continuous until detachment. Different oxidation conditions also affect the oxidation behavior：as the temperature increases，the oxidation rate of the alloy accelerates，and the thickness of the oxide layer also increases. When loaded applied，the dislocations in the γ matrix increase and aggregate at the interface of γ and γ′ phases，accelerating the outward diffusion rate of Al elements and causing the growth of the oxide layer to accelerate. The oxidation behavior also show anisotropy，specifically，the oxidation resistance of （100） surface is worse than that of （110） surface. This difference may be attributed to the distinct growth structures of oxide on various oriented surfaces，leading to different numbers of short-circuit diffusion paths on the surface，or may be caused by varying diffusion path lengths at the two-phase interfaces in different orientations. The differences in antioxidant properties can also be explained from the perspective of atomic adsorption. First-principles calculations show that different oriented surfaces have different adsorption capacities for oxygen atoms，which lead to the anisotropy of oxidation. The higher the surface roughness is，the more dislocations and defects are near the surface. These defects provide outward diffusion channels for Al ions，rapidly generate a dense alumina layer and improve the antioxidation performance of the alloy. In the future，research on the oxidation of single crystal superalloys can be carried out from the following directions： （1） Utilize in-situ oxidation technology with longer coverage time，more accurate stress-temperature control，and finer observation to establish a more precise oxidation model. （2） Use more high-precision instruments to characterize trace rare earth elements and explore its modification mechanism deeply to achieve precise and efficient doping of rare earth elements. （3） Carry out the research on the multi-factor synergy，coupling two or more conditions to study the oxidation behavior of alloys closest to actual service environment，thus establishing an oxidation model more in line with real situations. （4） Conduct research on the influence of oxidation behavior on alloy creep/fatigue fracture behavior. In-depth study of the relationship between oxidation and mechanical performance such as creep and fatigue are helpful to deepen the understanding of material deformation and failure behavior and improve the service life of components.

Copper anode slime contains many valuable metals such as silver，copper，selenium，tellurium，lead and gold，which is an important raw material for the production of gold，silver，selenium，tellurium and other precious metals and scattered metals. Due to the technology of microwave heating had many advantages，such as selective heating，fast heating speed，high heating efficiency，good heating uniformity and so on，hence copper anode slime of removing arsenic and antimony as raw material was studied the effects of steaming selenium conditions on selenium volatilization rate under different microwave heating conditions of roasting time，roasting temperature and ratio of acid to ore，and the optimum process conditions were also determined. The content of selenium in steamed selenium residue was analyzed by inductively coupled plasma atomic emission spectrometer （ICP-AES）. The existing forms and characteristics of main minerals in the sample were analyzed by X-ray diffractometer （XRD），scanning electron microscope and energy dispersive spectrometer （SEM-EDS）. The kinetics of sulfation roasting of copper anode slime heated by microwave was studied by the shrinking unreacted core model of gas-solid phase reaction at 673~823 K. The total experimental results showed that the conditions of increasing the roasting temperature，prolonging the roasting time and increasing the acid-ore ratio of acid to ore were beneficial to increase the volatilization rate of selenium，because the increase of above conditions could promote the positive reaction of selenium evaporation reaction. The temperature conditions’ results showed that the rate of selenium volatilization increased with the increase of temperature，whereas tended to rise slowly at 823 K，with the greatest rate of selenium volatilization was 94.49%. The time factors’ results showed that sulfuric acid was sufficient at the early stage of steaming selenium，which promoted the reaction of steaming selenium. However，when the time of the selenium steaming reached 45 min，the volatilization rate of selenium tended to rise gradually，and the optimal volatilization rate of selenium was 94.49%. The conditions of ratio of acid to ore results showed that when the ratio of acid to ore was relatively low，that was the amount of sulfuric acid was insufficient，hence the reaction of selenium and selenides with concentrated sulfuric acid to form SeO₂ was incomplete. With the increase of ratio of acid to ore，the contact area between sulfuric acid and material increased，which could make the steaming selenium reaction proceed rapidly. With the ratio of acid to ore of 0.85，the evaporation selenium reaction was basically complete，and the selenium volatilization rate of 96.83% could be obtained. Under the optimum conditions of air flow rate of 200 L·h⁻¹，roasting temperature of 823 K，roasting time of 45 min and the ratio of acid to ore of 0.85，the selenium content in steamed selenium slag was decreased from 6.43% to 0.17%，and the volatilization rate of selenium reached 96.83%. Selenium mainly existed in the form of CuSe₂，CuSe，Cu₂Se and NiSe in copper anode slime，and no characteristic peak of selenium compounds was observed in steamed selenium slag，indicating that selenium was volatilized thoroughly. Steamed selenium slag was mainly composed of AgCl，BaSO₄，PbSO₄，CuO，CuSO₄，NiSO₄ and other compounds. The selenium volatilization rate obtained at the roasting temperature of 673~823 K and the roasting time of 35~50 min was introduced into the shrinking unreacted core model of the gas-solid phase reaction，respectively，and the relationship between and time t was obtained. The relationship diagrams between lnk (k is the rate constant) and 1000/T (T is the temperature) under different temperatures was obtained according to the slope of each fitting line in the diagram. The apparent activation energy of sulfation and evaporation of selenium by microwave heating of copper anode slime was calculated as 41.830 kJ∙mol⁻¹ by Arrhenius formula，and the pre-exponential factor was 3.319，indicating that the process of selenium evaporation was controlled by chemical reaction. The kinetic equation was as follows：$1-{\left(1-x\right)}^{1/3}=3.319\times \exp \left(\frac{-41.830}{RT}\right)\times t$, where x is the volatilization rate of selenium, t is the roasting time, R is the gas constant.

In recent years，gallium-based liquid alloys had been widely used as coolants in nuclear reactor cooling systems and in concentrating solar energy，as well as lubricants in bearing systems，due to their good fluidity and high thermal conductivity，which had greatly improved the efficiency and performance of these devices. Therefore，it was of great importance to understand the rheological characteristics of liquid gallium-based alloys. Because the rotation method could measure the viscosity at different shear rate，many researchers measured the rheological properties of gallium-based liquid metals by the rotation method and obtained many valuable results. However，due to the high surface tension，high density and low viscosity of gallium-based liquid metal，it was difficult to obtain a relatively stable viscosity value by the rotation method. Therefore this work designed a viscometer with a rotating outer cylinder and Mo central rotator to measure the viscosity of gallium-based liquid metal. The rheological properties of oxidized and unoxidized Ga_66.7In₂₀Sn_13.3（mass fraction） liquid metals in a wide range of shear rates （0~120 s⁻¹） were measured. Ga_66.7In₂₀Sn_13.3 liquid metal was obtained by heating gallium，indium and tin （all 99.999% purity） in argon atmosphere （O²<0.25×10⁻⁶） to 200 ℃ for 4 h. The melting points of gallium，indium and tin were 30，156.6 and 231.9 ℃，respectively. The ternary eutectic Ga_66.7In₂₀Sn_13.3 alloy had a melting point of 10.6 ℃. The coaxial cylinder rotary viscometer （NDJ-5S，Lichen，Shanghai） was used，and the quartz outer cylinder （30 mm in the inner diameter） was driven by the motor and rotates at a speed of （0~306 r·min⁻¹）. A pure molybdenum inner rotator with a diameter of 20 mm and a height of 50 mm was used to overcome the buoyancy of liquid metal and enhance the stability of the rotor. The measurement was carried out based on the Couette principle. According to the different rheological laws of Newtonian fluid and non-Newtonian fluid，an approximate shear rate conversion method was used to convert the shear rate of non-Newtonian fluid into that of Newtonian fluid，and the rheological relationship between τ and $\dot{\gamma }$ was determined in both oxidized gallium-based liquid metal cases and non-oxidized gallium-based liquid metal cases. The results indicated that at a low shear rate，the viscosity of the oxidized liquid metal reached 60 mPa·s. With the increase of shear rate，the viscosity gradually decreased. When the shear rate increased above 30 s⁻¹，the viscosity gradually tended to be stable value with a minimum of 7.27 mPa·s. However，the viscosity of non-oxidized liquid metal remained at 4.51 mPa·s as the shear rate varied. The results also showed that the rheological relationship of the oxidized Ga_66.7In₂₀Sn_13.3 was $\tau =27.37{\dot{\gamma }}^{0.69}$，and the rheological relationship of unoxidized Ga_66.7In₂₀Sn_13.3 was $\tau =4.51\dot{\gamma }+4.08$. The oxidized liquid metal exhibited the characteristics of pseudoplastic non-Newtonian fluid and the unoxidized liquid metal exhibited the characteristics of Newtonian fluid. The pseudoplasticity of the oxidized liquid metal came from the elasticity of gallium oxide，which had the elastic properties similar to that of a solid and was the source of the non-Newtonian properties of the gallium-based liquid metal. Accordingly，the appearance viscoelastic of gallium-based liquid metal were made of the viscous force of liquid metal flow and the elastic deformation force of oxide film. With the increase of shear rate，the elastic force of gallium oxide reached an maximal yield stress，and the liquid metal viscosity tended to be stable.

The development and use of fossil energy not only promote the development of global economy，but also bring two major crises to human beings: environmental pollution and energy exhaustion. Based on this，the use of new energy，looking for green and efficient new energy conversion technology has become the focus of research. Photocatalysis，as a new green energy conversion technology，converts solar energy into chemical energy that can be directly used，which has been widely concerned by researchers. The principle of this technology is put forward by the solid energy band theory，that is，when the light with energy greater than the semiconductor band gap shines on the surface of the catalyst，the electrons in the valence band will be excited to jump to the conduction band，leaving a hole in the valence band. These holes and electrons can directly with the target molecule，can also with the catalyst surface adsorption of O₂ and H₂O or OH ⁻ reaction，generate reactive free radicals，and participate in the reaction. Due to the direct use of solar energy，photocatalytic technology has low consumption，clean and other innate advantages. At present，this technology has shown great application potential in the purification of environmental pollutants and the development of clean energy. In order to obtain higher conversion efficiency，the research on catalytic mechanism and structural modification of materials has become a hot topic in physical chemistry，materials science and environmental chemistry. The low e-h separation efficiency of catalyst materials is the main bottleneck hindering the practical application of photocatalytic technology. Among them，the construction of composite materials is considered to be one of the most effective ways to develop highly active photocatalysts. On the one hand，the composite catalyst can combine the advantages of different materials into one，thus significantly expanding its application range. On the other hand，the carrier can migrate to the surface of different components，which can effectively improve the separation efficiency of photogenerated charge through physical isolation.Among many semiconductor materials，tungsten trioxide （WO₃） is popular because of its good visible light response （band gap around 2.70 eV） and excellent valence band hole oxidation ability. Driven by the pursuit of higher hole efficiency，a large number of WO₃ based composite photocatalysts have been constructed and reported，and their applications cover many fields. In order to make the design and application of WO₃ based composite photocatalytic materials more rational development，and to provide useful reference for peers，it is urgent to summarize and review relevant studies regularly. In this paper，the application and research progress of WO₃ based composite in photocatalysis in recent years are systematically summarized. Starting from structural characteristics of WO₃ itself，around the composite preparation methods and the characteristics of composite material structure and performance of structure-activity relationship between two hot issues were summarized，and finally expounds the existing WO₃ based composite photocatalyst in the decomposition of aquatic product hydrogen，CO₂ reduction，nitrogen fixation，and the application of pollutants removal in areas such as the status quo，and the prospects of the development prospect was put forward.

Numerous studies had shown that particle dispersion strengthening was an effective means to prepare high-performance copper matrix composites. 1%WC/Cu and 2%WC/Cu composites with uniform dispersion and distribution were prepared by adding a small amount of WC hard ceramic particles to copper powder by mechanical ball milling and combined with the vacuum hot pressing sintering process. The effect of sintering temperature on the microstructure and physical properties of the composites was also investigated. The microstructure observation mainly involved X-ray diffractometer （XRD），field emission scanning electron microscope （SEM） and transmission electron microscope （TEM）. The characterization of physical properties mainly included the determination of relative density，Vickers hardness，electrical conductivity，thermal conductivity and tensile strength. The results showed that：on the one hand，SEM image of the composite block demonstrated that WC particles were uniformly dispersed，and the uniformity did not change significantly with the increase of the sintering temperature，and the distribution of WC particles on the copper matrix after sintering still largely depended on the distribution of WC particles on the copper particles after ball milling. On the other hand，the high-resolution TEM image confirmed the existence of WC particles，and XRD patterns signified that the WC/Cu composite was composed of WC phase and Cu phase during the whole process，and the composite phase transition did not occur with the increase of sintering temperature，and the composite material was finally determined to be WC/Cu matrix composite material. Secondly，with the increase of sintering temperature，the relative density，electrical conductivity，thermal conductivity and Vickers hardness of WC/Cu-based sintered block gradually increased. When the sintering temperature increased from 975 to 1050 ℃，the relative density of 1%WC/Cu composite increased from 97.1% to fully dense （100%），and its Vickers hardness increased from HV 63.8 to HV 99.7，and the electrical conductivity increased from 98.3%IACS （International Annealed Copper Standard Resistivity） to 100%IACS，and the thermal conductivity at room temperature increased from 334.1 to 358.6 W·m⁻¹·K⁻¹. The relative density of 2%WC/Cu composite could also increase from 94.3% to fully dense （100%），and its Vickers hardness increased from HV 76.1 to HV 105.7，and its electrical conductivity also increased from 92.2%IACS to 100%IACS，and the thermal conductivity increased from 306.8 to 373.6 W·m⁻¹·K⁻¹. In fact，higher hot-pressing sintering temperature could improve the densification level of composites，and with the increase of the hot-pressing sintering temperature，the change trend of Vickers hardness，electrical conductivity and thermal conductivity of composite block was synchronized with the change trend of relative density to a certain degree，in which the corresponding increase in surface hardness was closely related to the degree of densification，and the degree of densification indirectly affected the change of electrical conductivity，while the change trend of thermal conductivity was almost the same as the change of electrical conductivity. Practically，it conformed to the Weidmann-Franz law that the thermal conductivity and electrical conductivity of metals were linearly proportional at room temperature. In addition，considering the limited strengthening effect of a single sintering process and the good plasticity of the composite block after hot pressing，the composite block at hot-pressing sintering temperature of 1050 ℃ was hot-rolled and composited. Comparing and observing cross-section TEM images of the samples before and after hot rolling，it could be seen that most of the dislocation fringes before hot rolling were distributed on the copper grains，and a few were distributed next to WC particles. Combined with the tensile curve before hot rolling，it could be judged that the sample had a plastic fracture model before hot rolling，which essentially indicated that the dislocation plugging effect under the Orowan strengthening mechanism before hot rolling was not fully exerted，and the tensile strength of the composite material was not fully realized，and the performance was more determined by the strength of the copper matrix itself. After hot rolling，it could be clearly seen that many dislocations surrounded the WC particles to form a plug，which was a typical feature of the Orowan mechanism to strengthen the matrix. Combined with the tensile curve after hot rolling，it could be judged that the sample had a brittle fracture model after hot rolling. This essentially indicated that the dislocation plugging effect under the Orowan strengthening mechanism after hot rolling was fully exerted，and the tensile properties of composites after hot rolling were more determined by the interface strength of the reinforcement/matrix. Therefore，the tensile strength of the final prepared 1%WC/Cu composite sample reached 407 MPa，and Vickers hardness reached HV 126.6，and the electrical conductivity could still maintain 99.1%IACS. The tensile strength of the final prepared 2%WC/Cu composite sample reached 405 MPa，Vickers hardness reached HV 124.1，and the electrical conductivity could still maintain 99.1%IACS.