A high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part and production method

Abstract

The present invention discloses a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part and a production method. Steps S0 to S4 are completed within 5 minutes. A copper alloy melt is poured into a vacuum-assisted die-casting device and injected into a mold cavity thereof. The injection molding is performed for 20-30 seconds before demolding. The high-performance Cu-Ni-Si-Cr alloy vacuum precision part is directly obtained, achieving near-net-shape forming of the high-performance Cu-Ni-Si-Cr alloy vacuum precision part. The present invention eliminates cold rolling and solution treatment, greatly improving the preparation speed and production efficiency. In addition, the second phase is reduced in size and more evenly distributed, and the grains are quasi-equiaxed and fine. The second phase is reduced in size and more evenly distributed, and the mechanical properties are greatly improved while maintaining electrical conductivity.

Description

Technical Field

[0001] The present invention relates to the technical field of high-performance Cu-Ni-Si-Cr alloy die-casting parts, in particular to a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part and a production method thereof. Background Art

[0002] High-performance copper alloys have attracted widespread attention due to their high strength and acceptable conductivity. High-performance copper alloys play an important role in the automation and electronics industries. However, the production process of high-performance copper alloys includes casting, homogenization treatment, solution treatment, cold rolling, aging treatment, stamping and machining. The traditional manufacturing of high-performance copper alloys requires a complex process flow, so it is necessary to improve it. Summary of the Invention

[0003] In view of the shortcomings of the existing technology, the purpose of the present invention is to provide a Cu-Ni-Si-Cr alloy and a production method, which eliminates cold rolling and solution treatment, greatly improves the preparation speed and production efficiency, and the grains are quasi-equiaxed and small, the size of the second phase is smaller and the distribution is more uniform, and the mechanical properties are greatly improved while maintaining the conductivity without loss.

[0004] In order to achieve the above object, the technical solution adopted by the present invention is:

[0005] A method for producing high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting parts, comprising the following steps:

[0006] Step S0, alloy smelting treatment, performing a first smelting of the metal raw material by vacuum induction melting to obtain a copper alloy melt, wherein the mass percentages of the components of the metal raw material are 3-4% nickel, 0.5-0.8% silicon, 0.2-0.3% chromium, and the balance copper;

[0007] Step S1: vacuum preheating the mold, vacuuming and preheating the cavity of the vacuum die-casting mold, preheating the mold to 250-280°C, and reducing the vacuum degree of the cavity to below 50Pa;

[0008] Step S2, pouring die-casting treatment, pouring the copper alloy melt obtained in step S0 into the injection cavity of a vacuum-assisted die-casting device, and then injecting the copper alloy melt in the injection cavity into the cavity of a vacuum die-casting mold through the vacuum-assisted die-casting device, and maintaining the die-casting pressure at 220-280 MPa;

[0009] Step S3, forming treatment, after holding the pressure for 20-30 seconds in step S3, the mold is opened, and the semi-finished copper alloy die-casting is obtained after demolding, so that the copper alloy die-casting is rapidly solidified in the atmosphere and forms a supersaturated solid solution, the alloy grains are refined and present a quasi-equiaxed morphology, and finally a uniformly distributed average grain size of 15±0.5μm is obtained.

[0010] Step S4, aging heat treatment, aging treatment is performed on the semi-finished vacuum die-casting part so that the secondary phase particles precipitated simultaneously in the copper matrix include a micron-scale strengthening phase with an average size of 1.1±0.5μm and a nano-scale strengthening phase with an average size of 8±0.5nm, thereby obtaining a finished high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part.

[0011] For die-cast parts with a total mass of less than 10 kg, steps S0 to S3 are completed within 5 minutes, and near-net forming of high-performance Cu-Ni-Si-Cr alloy vacuum precision parts is achieved.

[0012] In a further technical solution, the copper is selected from high-purity cathode copper with a purity of 99.99%, the nickel is selected from high-purity nickel beads with a purity of 99.99%, the silicon is selected from high-purity silicon wafers with a purity of 99.99%, and the chromium is selected from high-purity chromium particles with a purity of 99.9%.

[0013] The Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part is Cu-3.18Ni-0.75Si-0.28Cr in percentage by mass.

[0014] In a further technical solution, in step S4, the size of the phase particles of the precipitated nano-scale reinforcement phase is 8 nm, and the spacing between the precipitated phases of the nano-scale reinforcement phase is 10 nm.

[0015] In a further technical solution, in step S4, the precipitated secondary phase particles are nano-sized phase particles of δ-Ni2Si phase, and the orientation relationship between the δ-Ni2Si phase and the Cu matrix is ​​expressed as

[110] Cu ||

[100] δ .

[0016] In a further technical solution, the high-performance Cu-Ni-Si-Cr alloy vacuum precision die-cast parts have a spherical second phase with an average size of 1.1±0.5 μm and a short rod second phase with an average length of 2.3±0.4 μm evenly distributed in their structure.

[0017] In a further technical solution, the total die-casting time from the alloy smelting process in step S0 to the forming process in step S3 and the injection holding time of the forming process in step S3 are controlled relative to the total weight of the total mass of the die-cast part according to the following corresponding relationship:

[0018] The total mass of the die-cast parts is less than 1kg, the total die-casting time is 2 minutes, and the molding process injection and pressure holding time is 10 seconds.

[0019] The total mass of the die-cast parts is 1-5kg, the total die-casting time is 3 minutes, and the molding process injection and holding time is 15 seconds.

[0020] The total mass of the die-cast parts is 8-10kg, the total die-casting time is 5 minutes, and the molding process injection and holding time is 20 seconds.

[0021] The total mass of the die-cast parts is 10-30kg: the total die-casting time is 5-6 minutes, and the molding process injection and pressure holding time is 25 seconds.

[0022] The total mass of the die-cast parts is 30-50kg: the total die-casting time is 6-8 minutes, and the molding process injection and pressure holding time is 30 seconds.

[0023] In a further technical solution, in step S1, the mold is preheated to 260° C. and the vacuum degree of the cavity is reduced to below 30 Pa;

[0024] In step S2, the pouring temperature of the copper alloy melt is controlled at 1250°C, the die-casting pressure of the copper alloy melt is controlled at 220 MPa, fast shot die-casting is used in the middle and early stages of die-casting, and the fast shot speed of the fast shot die-casting is controlled at 1.6 m / s. In the later stages of die-casting, slow shot die-casting is used, and the slow shot speed of the slow shot die-casting is controlled at 0.3 m / s.

[0025] In a further technical solution, the die casting pressure of step S2 and the injection holding time of step S3 are set and controlled.

[0026] According to the following formula, the solute diffusion coefficient D and the die casting pressure P are set.

[0027]

[0028] In the formula, P is the die casting pressure, D is the solute diffusion coefficient, R is the gas constant, T is the temperature, δ is the atomic free path length, η0 is the viscosity of the melt at normal pressure, and V0 is the initial volume of the liquid phase;

[0029] At the same time, the grain growth rate U is set according to the following formula to control the copper alloy melt to maintain a high cooling rate during the solidification forming process and keep it in a non-equilibrium state, so as to promote solid solution, limit grain growth and refine secondary phase particles.

[0030]

[0031] In the formula, U is the grain growth rate, f is the interface coefficient factor, D is the solute diffusion coefficient, ΔG is the free energy difference between the two phases, R is the gas constant, T is the temperature, and a is the interatomic distance.

[0032] In a further technical solution, step S2 adopts a rapid pressurized filling counter-gravity casting method, wherein the copper alloy melt injected into the vacuum die-casting mold is filled from the bottom of the cavity by vacuum-assisted die-casting equipment and rapidly pressurized to the top of the cavity, so that during the upward movement of the copper alloy melt, the high-temperature melt is in continuous contact with the inner wall of the mold that has just been cooled, thereby increasing the heat transfer rate and accelerating the cooling rate;

[0033] The heat exchange between the die-cast part and the cavity interface is set and controlled by the following formula, and the injection holding time t is set to 20S.

[0034]

[0035] In the formula, h is the interface heat transfer coefficient, Q is the heat passing through the interface, q is the interface heat flux, A is the contact area between the die casting and the cavity, t is the injection holding time, and ΔT is the temperature difference between the die casting surface and the cavity surface.

[0036] A Cu-Ni-Si-Cr alloy vacuum precision die-cast part is prepared according to the above-mentioned production method of a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-cast part. The Cu-Ni-Si-Cr copper-gold vacuum precision die-cast part is Cu-3.18Ni-0.75Si-0.28Cr by weight.

[0037] The advantages of the present invention compared with the prior art are:

[0038] 1. Omit the two important steps of cold rolling and solid solution in the traditional copper alloy preparation process. Use vacuum die casting and take advantage of its sub-rapid solidification characteristics to keep the die-cast alloy in a high solid solution state. Direct aging treatment is then performed to precipitate the second phase and improve the alloy performance.

[0039] 2. Achieve rapid preparation and complete alloy forming within five minutes, greatly improving production efficiency.

[0040] 3. Compared with traditional casting alloys, the grain size of the vacuum die-casting alloy of the present invention is significantly refined, the size of the second phase is smaller, and the distribution is more uniform.

[0041] 4. The vacuum die-casting of the present invention eliminates the dendrite segregation phenomenon produced during casting, so that the alloy elements are evenly distributed, which helps to uniformly precipitate the second phase during subsequent aging treatment and improves the overall performance. BRIEF DESCRIPTION OF THE DRAWINGS

[0042] Figure 1 This is the grain metallographic diagram of Example 1.

[0043] Figure 2 This is the grain metallographic diagram of Example 2.

[0044] Figure 3 This is the grain metallographic diagram of Example 3.

[0045] Figure 4 This is the grain metallographic diagram of Example 4.

[0046] Figure 5 This is the grain metallographic diagram of Comparative Example 1.

[0047] Figure 6 These are optical microscopic morphologies of the samples of Example 1 and Comparative Example 1 before heat treatment.

[0048] Figure 7 The SEM morphology images and EDS element distribution images of the samples of Example 1 and Comparative Example 1 after heat treatment.

[0049] Figure 8 This is a TEM photograph of the nano-precipitated phase in Example 1.

[0050] Figure 9 The SEM image and EDS element analysis of the segregation elements of Comparative Example 1 are shown.

[0051] Figure 10 This is a simulation diagram of the vacuum die-casting solidification process of Examples 1-4.

[0052] Figure 11 These are the physical image and metallographic diagram of the alloy prepared in Example 1.

[0053] Figure 12 a is a schematic diagram of the formation and growth of externally solidified crystals ESCs.

[0054] Figure 12 b Schematic diagram of temperature and grain distribution of VADC alloy.

[0055] Figure 12 c Melt cooling curves in different regions obtained by simulating the temperature field of the VADC process.

[0056] Figure 12 dSupersaturated solid solution.

[0057] Figure 12eSchematic diagram of the hindering effect of grain boundaries on electron movement. DETAILED DESCRIPTION

[0058] Example 1

[0059] A method for producing high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting parts, comprising the following steps:

[0060] The total mass of the metal raw material is 10 kg. The copper alloy melt is then poured into a vacuum cold chamber die-casting machine for die-casting, and steps S0 to S4 are completed within 5 minutes, and the near-net shape of the high-performance Cu-Ni-Si-Cr alloy vacuum precision part is achieved, and the finished product high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-cast part 1# sample is obtained, as follows.

[0061] Step S0, alloy smelting, involves first smelting the metal raw materials via vacuum induction melting to produce a copper alloy melt. The weight percentages of the metal raw materials are as follows: 3-4% nickel, 0.5-0.8% silicon, 0.2-0.3% chromium, and the balance copper. The copper is 99.99% pure high-purity cathode copper, the nickel is 99.99% pure high-purity nickel beads, the silicon is 99.99% pure silicon wafers, and the chromium is 99.9% pure high-purity chromium granules.

[0062] Step S1: vacuum preheating the mold, vacuuming and preheating the cavity of the vacuum die-casting mold, preheating the mold to 260°C, and reducing the vacuum degree of the cavity to below 30Pa;

[0063] Step S2, pouring die-casting treatment, pouring the copper alloy molten liquid obtained in step S0 into the injection cavity of the vacuum-assisted die-casting equipment, and then casting the copper alloy molten liquid in the injection cavity into the cavity of the vacuum die-casting mold through the vacuum-assisted die-casting equipment, controlling the pouring temperature of the copper alloy molten liquid at 1250°C, and controlling the die-casting pressure of the copper alloy molten liquid at 220 MPa. In the middle and early stages of die-casting, fast shot die-casting is used, and the fast shot speed of the fast shot die-casting is controlled at 1.6 m / s. In the later stages of die-casting, slow shot die-casting is used, and the slow shot speed of the slow shot die-casting is controlled at 0.3 m / s.

[0064] Step S3, forming treatment, after holding the pressure for 20-30 seconds in step S3, the mold is opened, and the semi-finished copper alloy die-casting is obtained after demolding, so that the copper alloy die-casting is rapidly solidified in the atmosphere and forms a supersaturated solid solution, the alloy grains are refined and present a quasi-equiaxed morphology, and finally a uniformly distributed average grain size of 15±0.5μm is obtained.

[0065] Step S4, aging heat treatment, aging treatment is performed on the semi-finished vacuum die-casting part so that the secondary phase particles precipitated simultaneously in the copper matrix include a micron-scale strengthening phase with an average size of 1.1±0.5μm and a nano-scale strengthening phase with an average size of 8±0.5nm, thereby obtaining a finished high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part; the Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part is Cu-3.18Ni-0.75Si-0.28Cr by mass percentage.

[0066] Specifically, the size of the precipitated nano-scale strengthening phase particles is 8 nm, and the spacing between the precipitated nano-scale strengthening phase particles is 10 nm. The precipitated secondary phase particles are nano-scale phase particles and are δ-Ni2Si phases. The orientation relationship between the δ-Ni2Si phase and the Cu matrix is ​​expressed as

[110] Cu ||

[100] δ The crystals of high-performance Cu-Ni-Si-Cr alloy vacuum precision die-cast parts are uniformly distributed with a second phase in the shape of spheres with an average size of 1.1±0.5μm and a second phase in the shape of short rods with an average length of 2.3±0.4μm.

[0067] Example 2

[0068] The production process of this embodiment is the same as that of embodiment 1, except that in step S2, the pouring temperature of the copper alloy melt is controlled at 1150°C to prepare a finished high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part 2# sample. At this time, a large-sized pressure chamber pre-crystallization structure ( Figure 2 ).

[0069] Example 3

[0070] The production process of this embodiment is the same as that of Example 1, except that in step S2, the pouring temperature of the copper alloy melt is controlled at 1200°C to prepare a finished high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part 3# sample. At this time, a large-sized pressure chamber pre-crystallization structure ( Figure 3 ).

[0071] Example 4

[0072] The production process of this embodiment is the same as that of Example 1, except that in step S2, the pouring temperature of the copper alloy melt is controlled at 1300°C to prepare a finished high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-casting part 4# sample. At this time, a large-sized pressure chamber pre-crystallization structure ( Figure 4 ).

[0073] Comparative Example 1

[0074] The raw metal was first melted using vacuum induction melting to produce a molten metal. The weight percentages of the raw metal components were 3-4% nickel, 0.5-0.8% silicon, 0.2-0.3% chromium, and the balance copper. The molten metal was then poured into a steel mold and furnace-cooled for 8 hours. Finally, the casting was solution treated at 980°C for 2 hours and aged at 500°C for 5 hours to produce sample 5 of the high-performance Cu-Ni-Si-Cr copper alloy vacuum precision die-cast part.

[0075] Physical property tests and conductivity tests were performed on samples #1 to #5. See Table 1 for sample performance test table for details.

[0076]

[0077]

[0078] Table 1 - Sample performance test table

[0079] The process of comparative example 1 is a traditional process, referred to as VAC process, and the copper alloy prepared in comparative example 1 is referred to as VAC alloy; the process of the present invention is referred to as VADC process, and the Cu-Ni-Si-Cr alloy vacuum precision die-casting part prepared in example 1 is referred to as VADC alloy.

[0080] Obviously, the entire forming cycle of the parts (VAC alloy) of the traditional casting process is at least 15 hours, while the present invention reduces the entire die-casting forming cycle of the parts (VADC alloy) to 5 minutes, significantly increasing the production speed, improving production efficiency, and saving energy and reducing consumption. At the same time, the Cu-Ni-Si-Cr copper alloy vacuum precision die-cast parts prepared by the present invention have better mechanical properties, as shown in Table 1, including tensile strength, elongation and hardness, and have good electrical conductivity. This performance enhancement is mainly due to the faster solidification rate and finer grain size of the VADC alloy. Under pressure conditions, better contact is formed between the molten metal and the mold, and frequent heat exchange leads to a quenching treatment effect in the VADC alloy. This leads to the formation of a supersaturated solid solution. The DA treatment causes nano-scale precipitates to precipitate in the VADC alloy, thereby improving the mechanical properties and electrical conductivity of the VADC alloy.

[0081] Due to the limitations of solid-state forming processes, especially due to the significant solidification shrinkage and limited fluidity of high-melting-point metals such as copper alloys, it is impossible to omit important steps such as cold rolling and solution treatment in the existing process and directly cast to obtain high-performance copper alloy vacuum precision die-cast parts. The present invention studies the organizational evolution and performance enhancement mechanism of Cu-Ni-Si-Cr alloy under specific heat treatment conditions, simplifies the production process, and achieves near-net forming of high-performance Cu-Ni-Si-Cr alloy vacuum precision parts. A direct aging vacuum-assisted die casting process (VADC) that eliminates important steps such as cold rolling and solution treatment is used to prepare high-performance Cu-Ni-Si-Cr alloy vacuum precision parts obtained by direct casting. The process of the present invention omits the important steps of cold rolling and solution treatment in the existing casting process, performs high-pressure die casting under a vacuum environment and reduces gas inclusions in the casting, while accelerating the solidification rate of the casting. The high-performance Cu-Ni-Si-Cr alloy vacuum precision parts obtained by direct casting have smaller grain size, less porosity and more uniform composition. Figure 11 This is the actual image and metallographic diagram of the vacuum-assisted die-cast Cu-3.18Ni-0.75Si-0.28Cr (wt%) alloy of Example 1.

[0082] The formation mechanism of externally solidified crystals ESCs in VADC alloys is as follows Figure 12 As shown in a, the pre-nucleated external solidification crystals (ESCs) are squeezed into the cavity under pressure, and the molten metal begins to solidify around the external solidification crystals (ESCs). Since the external solidification crystals (ESCs) nucleate earlier and grow longer, their size tends to be larger. Figure 1 As shown. By optimizing the casting process, a uniform grain structure of the die casting is achieved. Figure 11 As shown. The VADC process of the present invention is a counter-gravity casting process that involves the rapid pressurized filling of copper alloy melt from bottom to top. During the upward movement, the hot melt is in continuous contact with the freshly cooled mold wall, which enhances heat transfer and accelerates cooling. This interaction gradually reduces the temperature of the melt. The heat transfer behavior of the die-cast part and the cavity interface can be measured by the heat transfer coefficient.

[0083]

[0084] In the formula, h is the interface heat transfer coefficient, Q is the heat passing through the interface, q is the interface heat flux, A is the contact area between the die casting and the cavity, t is the injection holding time, and ΔT is the temperature difference between the die casting surface and the cavity surface. The heat transfer coefficient quantifies the amount of heat transferred through the interface between the die casting and the cavity per unit area, per unit time, and per unit temperature gradient. This coefficient is crucial in determining the efficiency of heat exchange between the casting and the cavity, thereby affecting the microstructure of the VADC alloy. This significant and rapid heat exchange results in a significant refinement of the grain size of the VADC alloy, Figure 12 The present invention uses numerical simulation software to simulate the temperature changes in areas I, II and III. The specific temperature field changes are as follows Figure 10 The results show that the temperature of VADC alloy increases gradually from zone Ⅰ to zone Ⅲ. Figure 12 c. In addition, the heat transfer coefficient of VADC decreases gradually from top to bottom, resulting in a higher solidification rate at the top of the mold cavity than at the bottom. This temperature gradient results in a slightly finer grain size in the upper part of the alloy compared to the bottom of the VADC alloy. Figure 12 b and Figure 11 As shown, the VADC method is therefore conducive to a faster heat transfer rate between the melt and the mold wall, which leads to rapid quenching of the melt and the formation of a supersaturated solid solution. Figure 12 d. The high solid solution structure leads to a decrease in the as-cast properties of the VADC alloy. In this high-energy metastable state, direct aging treatment of the VADC alloy can induce the precipitation of nano-strengthening phases, thereby improving the comprehensive properties of the VADC alloy. However, due to the fine grain size of the VADC alloy, the scattering effect of the grain boundary on electrons increases, resulting in a decrease in the electrical conductivity of the VADC alloy relative to the VAC alloy. Figure 12 As shown in e.

[0085] Due to the slow cooling rate of the melt, VAC alloy will have large grains with a size of more than 400μm before thermal aging treatment. Figure 5 At the same time, a coarse dendritic structure is formed in the VAC alloy of the VAC process of Comparative Example 1, which is usually accompanied by obvious microsegregation of alloy elements. Figure 5 As shown, Figure 9 The microsegregation elements in the dendrites are Ni and Si. However, due to the extremely fast solidification speed of the VADC alloy under pressure, the grain size formed is small, about 15μm. Figure 1 shown.

[0086] Due to the slow cooling rate of VAC alloy, the size of micron-scale primary phase is larger during the solidification process of the alloy, and the size is about 4.3±0.7μm. Figure 7As shown in a. The micron-sized primary phase of the alloy prepared by the VADC process is mainly spherical with an average size of about 1.1±0.5μm, and some are short rods with an average length of about 2.3±0.4μm. Figure 7 As shown in b.

[0087] In the VADC process of the present invention, the molten alloy is forced into the mold, which accelerates solidification and minimizes the tendency of dendrite segregation, so that the grains in the VADC alloy are significantly refined and present a quasi-equiaxed morphology. Figure 1 As shown. The VADC process of the present invention achieves a higher solidification pressure P, resulting in a lower solute diffusion coefficient D, and thus maintaining the solid solution state of the alloy elements in the alloy liquid during the solidification process. During the solidification process, the pressure reduces the interatomic distance α and the diffusion coefficient D, resulting in a decrease in the grain growth rate U, which ultimately limits the grain growth and leads to grain refinement. At the same time, the high cooling rate puts the VADC alloy in a non-equilibrium state, promotes solid solution, refines the secondary phase particles, and limits grain growth. A large number of secondary phase particles are precipitated in the Cu-Ni-Si-Cr alloy after heat treatment. Compared with the VAC alloy, the micron-sized precipitated phase in the VADC alloy is smaller in size and more evenly distributed. Figure 7 The morphology and crystallographic characteristics of the nanoscale precipitates in the VADC alloy after thermal aging treatment are shown in Figure 2. Figure 8 As shown. Figure 8 It can be seen from the TEM bright field image that after direct aging treatment at 450℃ for 6 hours, the supersaturated solid solution precipitated secondary phase particles in the grain boundaries. There is a coherent relationship between the precipitated secondary phase particles and the matrix. The secondary phase particles cause distortion of the nearby matrix, resulting in a characteristic contrast effect. When observing the precipitated phase of the

[110] Cu band axis under the central dark field TEM image, it is found that the secondary phase particles are spherical. The size of the precipitated secondary phase particles is about 8±2nm, and the spacing between the precipitated phases is about 10nm. The fast Fourier transform (FFT) of the secondary phase particles is as follows: Figure 8 The results show that the nanoscale phase particles in the VADC alloy are δ-Ni2Si phase, and the orientation relationship between the δ-Ni2Si phase and the Cu matrix can be expressed as

[110] Cu ||

[100] δ The uniform and fine nano-scale precipitation phase ensures the ideal strengthening effect and ensures that the alloy has excellent mechanical properties.

Claims

1. A method for producing high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting parts, characterized by: The following steps are included: Step S0, alloy smelting treatment, performing a first smelting of the metal raw material by vacuum induction melting to obtain a copper alloy melt, wherein the mass percentages of the components of the metal raw material are 3-4% nickel, 0.5-0.8% silicon, 0.2-0.3% chromium, and the balance copper; Step S1: vacuum preheating of the mold, vacuuming and preheating the cavity of the vacuum die-casting mold, preheating the mold to 250-280°C, and reducing the vacuum degree of the cavity and the pressure chamber to below 50Pa; Step S2, pouring die-casting treatment, pouring the copper alloy melt obtained in step S0 into the injection cavity of a vacuum-assisted die-casting device, and then injecting the copper alloy melt in the injection cavity into the cavity of a vacuum die-casting mold through the vacuum-assisted die-casting device, and maintaining the die-casting pressure at 220-280 MPa; Step S3, forming treatment, after holding the pressure for 20-30 seconds in step S3, the mold is opened, and after demolding, a semi-finished copper alloy die casting is obtained, and the copper alloy die casting is rapidly solidified in the atmosphere to form a supersaturated solid solution, and the alloy grains are refined and present a quasi-equiaxed morphology, and finally a uniformly distributed average grain size of 15±0.5 μm is obtained; Set and control the die casting pressure in step S2 and the injection holding time in step S3. According to the following formula, the solute diffusion coefficient D and the die casting pressure P are set. In the formula, P is the die casting pressure, D is the solute diffusion coefficient, R is the gas constant, T is the temperature, δ is the atomic free path length, η0 is the viscosity of the melt at normal pressure, and V0 is the initial volume of the liquid phase; At the same time, the grain growth rate U is set according to the following formula to control the copper alloy melt to maintain a high cooling rate during the solidification forming process and keep it in a non-equilibrium state, so as to promote solid solution, limit grain growth and refine secondary phase particles. In the formula, U is the grain growth rate, f is the interface coefficient factor, D is the solute diffusion coefficient, ΔG is the free energy difference between the two phases, R is the gas constant, T is the temperature, and a is the interatomic distance; Step S4, aging heat treatment, performing aging treatment on the semi-finished vacuum die-casting part, so that the secondary phase particles precipitated simultaneously in the copper matrix include micron-scale strengthening phases with an average size of 1.1±0.5 μm and nano-scale strengthening phases with an average size of 8±0.5 nm, thereby obtaining a finished high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part; For die-cast parts with a total mass of less than 10 kg, steps S0 to S3 are completed within 5 minutes, and near-net forming of high-performance Cu-Ni-Si-Cr alloy vacuum precision parts is achieved.

2. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: The copper is selected from high-purity cathode copper with a purity of 99.99%, the nickel is selected from high-purity nickel beads with a purity of 99.99%, the silicon is selected from high-purity silicon wafers with a purity of 99.99%, and the chromium is selected from high-purity chromium particles with a purity of 99.9%. The Cu-Ni-Si-Cr alloy vacuum precision die-casting part comprises Cu-3.18Ni-0.75Si-0.28Cr in percentage by mass.

3. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: In step S4, the size of the precipitated nano-scale reinforcement phase particles is 8 nm, and the spacing between the precipitated nano-scale reinforcement phase particles is 10 nm.

4. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: In step S4, the precipitated secondary phase particles are nano-sized phase particles of δ-Ni2Si phase, and the orientation relationship between the δ-Ni2Si phase and the copper matrix is ​​expressed as [110] Cu ||[100] δ .

5. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: The high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part has uniformly distributed therein a second phase in the shape of a sphere with an average size of 1.1±0.5 μm and a second phase in the shape of a short rod with an average length of 2.3±0.4 μm.

6. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: The total die-casting time from the alloy smelting process in step S0 to the molding process in step S3 and the injection holding time of the molding process in step S3 are controlled relative to the total weight of the die-cast part according to the following corresponding relationship: The total mass of the die-cast parts is 8-10kg, excluding 10kg. The total die-casting time is 5 minutes, and the molding process injection and holding time is 20 seconds. The total mass of the die-cast parts is 10-30kg, excluding 30kg. The total die-casting time is 5-6 minutes, and the molding process injection and holding time is 25 seconds. The total mass of the die-cast parts is 30-50kg, excluding 50kg. The total die-casting time is 6-8 minutes, and the molding process injection and holding time is 30 seconds.

7. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: In step S1, the mold is preheated to 260° C. and the vacuum degree of the cavity is reduced to below 30 Pa; In step S2, the pouring temperature of the copper alloy melt is controlled at 1250°C, the die-casting pressure of the copper alloy melt is controlled at 220 MPa, fast shot die-casting is used in the middle and early stages of die-casting, and the fast shot speed of the fast shot die-casting is controlled at 1.6 m / s. In the later stages of die-casting, slow shot die-casting is used, and the slow shot speed of the slow shot die-casting is controlled at 0.3 m / s.

8. The method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-casting part according to claim 1, characterized in that: In step S2, a rapid pressurized filling counter-gravity casting method is used, wherein the copper alloy melt injected into the vacuum die-casting mold is filled from the bottom of the cavity and rapidly pressurized to the top of the cavity by vacuum-assisted die-casting equipment, so that during the upward movement of the copper alloy melt, the high-temperature melt is in continuous contact with the inner wall of the mold that has just been cooled, thereby increasing the heat transfer rate and accelerating the cooling rate; The heat exchange between the die-cast part and the cavity interface is set and controlled by the following formula, and the injection holding time t is set to 20S. In the formula, h is the interface heat transfer coefficient, Q is the heat passing through the interface, q is the interface heat flux, A is the contact area between the die casting and the cavity, t is the injection holding time, and ΔT is the temperature difference between the die casting surface and the cavity surface.

9. A Cu-Ni-Si-Cr alloy vacuum precision die-cast part, produced according to the method for producing a high-performance Cu-Ni-Si-Cr alloy vacuum precision die-cast part according to any one of claims 1 to 8, characterized in that: The Cu-Ni-Si-Cr alloy vacuum precision die-casting part comprises Cu-3.18Ni-0.75Si-0.28Cr by weight.

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