High-hardness anti-explosion beryllium copper alloy and preparation method thereof
By using multi-element microalloying and graded aging treatment, nanoscale precipitates and dense oxide films are formed, which solves the problems of decreased toughness and spark sensitivity of beryllium copper alloys after hardness improvement, and achieves a synergistic improvement in high hardness, impact resistance and explosion-proof performance.
Patent Information
- Authority / Receiving Office
- CN · China
- Patent Type
- Applications(China)
- Current Assignee / Owner
- DONGGUAN JIASHENG COPPER
- Filing Date
- 2026-05-27
- Publication Date
- 2026-07-14
Smart Images
Figure CN122382402A_ABST
Abstract
Description
Technical Field
[0001] This invention relates to the field of copper-based alloy materials technology, specifically to a high-hardness explosion-proof beryllium copper alloy and its preparation method. Background Technology
[0002] Beryllium copper alloys are widely used in explosion-proof tools and special-condition components due to their high strength, good electrical conductivity, and corrosion resistance. However, existing beryllium copper alloys still have the following shortcomings in practical applications: First, in the process of increasing hardness and strength, the toughness of the material decreases significantly, making it prone to local spalling during impact or friction; Second, under the traditional aging strengthening mechanism, the precipitated phase distribution is uneven, and continuous brittle phases easily form at grain boundaries, resulting in stress concentration under impact loads; Third, under friction or impact conditions, local high-temperature zones easily form on the material surface, leading to continuous spark generation and affecting explosion-proof safety.
[0003] Existing technologies typically improve performance through single strengthening or simple alloying methods, but it is difficult to achieve a good balance between high hardness, impact resistance, and explosion-proof properties. Therefore, it is necessary to develop a new beryllium copper alloy system and its preparation method to achieve synergistic improvement of multiple properties.
[0004] Patent CN112760521B discloses a beryllium copper alloy and a method for preparing the beryllium copper alloy. The above patent achieves high strength and stability while ensuring excellent elasticity, as well as high tensile strength, high electrical conductivity and excellent processing performance.
[0005] The beryllium copper alloy prepared by the above patent has high strength and stability. The beryllium copper alloy material obtained after cold plastic processing and solution aging treatment also has high tensile strength, high electrical conductivity and excellent processing performance. It has fast thermal conductivity, low coefficient of friction, easy machining, wear resistance, corrosion resistance, smoothness and long service life. However, the traditional strengthening methods for beryllium copper alloys are limited, and there are problems such as easy embrittlement after hardness improvement and excessive brittle phases at grain boundaries.
[0006] Therefore, this application proposes a high-hardness explosion-proof beryllium copper alloy and its preparation method, which establishes an alloy base that takes into account strengthening, refining and purification through the synergistic proportioning of multiple microalloying components. Summary of the Invention
[0007] The purpose of this invention is to provide a high-hardness explosion-proof beryllium copper alloy and its preparation method, so as to solve the technical problem mentioned in the background art of achieving a good balance between high hardness, impact resistance and explosion-proof performance.
[0008] To achieve the above objectives, the present invention provides the following technical solution: a high-hardness explosion-proof beryllium copper alloy, wherein the alloy comprises the following components by mass percentage:
[0009] Be 2.00-2.12%, Ni 1.18-1.38%, Co 0.60-0.82%, Cr 0.28-0.42%, Ti 0.045-0.065%, Zr 0.045-0.058%, Si 0.09-0.13%, Mg 0.018-0.028%, rare earth RE 0.008-0.015%, balance Cu and unavoidable impurities;
[0010] After solution treatment, cold deformation and graded aging, the average size of the matrix grains is 2-10 μm, the average grain size of the precipitates is 5-40 nm, and the length of the continuous brittle phase at the grain boundaries is no more than 20%, so as to form an explosion-proof structure with high hardness, low spark sensitivity and impact resistance.
[0011] Preferably, the rare earth RE is one or a combination of Ce and La, and the total content of Ce and La is 0.008-0.015%, wherein the mass ratio of Ce to La is 1:3-3:1. The rare earth RE is used to purify grain boundary inclusions, inhibit oxide film loosening and promote the formation of a continuous and dense composite passivation layer on the surface, thereby reducing the probability of the alloy igniting under friction or collision conditions.
[0012] Preferably, Ni, Co, and Be together form a composite precipitation strengthening system during the aging process, wherein the Ni-Be precipitate is the main strengthening phase, Co is used to stabilize the size and distribution of the precipitate, Cr, Ti, and Zr together inhibit abnormal grain growth and refine the grain boundary structure, and Si and Mg are used to improve the density and adhesion stability of the surface oxide film, so as to maintain impact toughness while improving hardness.
[0013] Preferably, after treatment, the alloy forms a composite dense oxide film with a thickness of 50-300 nm on its surface. The composite dense oxide film is enriched with Si, Mg and rare earth RE elements and is firmly bonded to the substrate. The composite dense oxide film is used to improve the surface's resistance to adhesive wear, reduce the local frictional heat concentration effect, and suppress the generation of continuous spark chains under impact conditions.
[0014] Preferably, the microstructure of the alloy satisfies the following: nanoscale precursor clusters and dispersed precipitates are uniformly distributed along the grain, and only intermittently distributed refined grain boundary phases are formed at the grain boundaries; the Vickers hardness of the alloy is 350-430 HV, and it still maintains a low hardness decay rate under repeated impact loads, so as to achieve a synergistic balance between high hardness and explosion-proof stability.
[0015] Preferably, the preparation method includes the following steps:
[0016] S1. Weigh the raw materials according to the mass percentage, melt them under vacuum or inert protective atmosphere, and then cast them into ingots after degassing and slag removal.
[0017] S2. Homogenize the ingot at 860-900℃ for 2-5 hours;
[0018] S3. The homogenized ingot is hot-worked at 780-830℃, with a total deformation of 60-80%.
[0019] S4. After hot working, the material is solution treated at 800-830℃ for 1-2 hours and then rapidly water quenched.
[0020] S5. Perform 10-25% cold deformation on the solution-treated material;
[0021] S6. After cold deformation, the material is pre-aged at 300-330℃ for 1-2 hours, and then peak aged at 430-460℃ for 1-1.5 hours.
[0022] S7. Finally, a low-temperature stabilization treatment is performed at 230-260℃ for 0.5-1 hour to obtain a high-hardness explosion-proof beryllium copper alloy.
[0023] Preferably, in step S1, a melting method combining low-frequency electromagnetic stirring and vacuum refining is used to make the melt composition distribution more uniform and reduce the oxygen content, sulfur content and non-metallic inclusion content; wherein, Be, Mg and rare earth RE are added in stages during the melting process to reduce volatilization loss and improve the solid solution efficiency of microalloying elements.
[0024] Preferably, the hot working in step S3 is carried out in a cross deformation manner. The cross deformation manner includes alternating hot rolling and hot forging, or changing the deformation direction of adjacent passes during multi-pass hot rolling. The cross deformation manner introduces high-density dislocations and breaks up the cast coarse dendrite structure, so as to provide uniform nucleation sites for subsequent precipitation strengthening.
[0025] Preferably, the pre-aging in step S6 is used to form nanoscale precursor clusters in the matrix, and the peak aging is used to transform the precursor clusters into a dispersed precipitate phase; wherein the pre-aging temperature is 310-325℃ and the time is 1-1.5 hours, and the peak aging temperature is 435-450℃ and the time is 1-1.2 hours, so as to control the size of the strengthening phase and avoid coarsening and embrittlement.
[0026] Preferably, after step S7, a surface stabilization treatment is also included. The surface stabilization treatment is carried out in an inert mixed atmosphere with an oxygen content of 1-8% at 180-230°C for 0.5-2 hours to promote the formation of a composite dense oxide film rich in Si, Mg and rare earth RE on the alloy surface. The composite dense oxide film works synergistically with the substrate to improve the anti-friction ignition capability and surface wear resistance stability under explosion-proof conditions.
[0027] Compared with the prior art, the beneficial effects of the present invention are:
[0028] 1. This invention establishes an alloy base that balances strengthening, refining and purification by synergistically proportioning multiple microalloying components. It solves the problems of traditional beryllium copper alloys having a single strengthening method, easy embrittlement after hardness increase, and excessive continuous brittle phases at grain boundaries. This allows the alloy to maintain high hardness while still having good toughness and impact adaptability, and reducing friction spark sensitivity.
[0029] 2. This invention solves the problems of coarse precipitates, uneven distribution, and severe local stress concentration in existing processes by eliminating segregation through solid solution, introducing dislocations through cold deformation, and controlling the size and distribution of precipitates through graded aging. It forms a microstructure in which fine grains, dispersed precipitates, and grain boundary discontinuity strengthening phases coexist, significantly improving hardness and microstructure stability, and enhancing impact resistance.
[0030] 3. This invention improves the grain boundary state and inhibits the formation of continuous brittle phases through grain boundary purification and brittle phase control technology, solving the problem that high-hardness beryllium copper is prone to intergranular cracking and local spalling under impact or repeated loading. The grain boundary continuity is better, the crack propagation path is more tortuous, the material is less likely to experience sudden aging under stress, and the overall service reliability is higher.
[0031] 4. This invention solves the problem of local high temperature points and continuous spark chains easily forming in materials under friction, collision or contact spark conditions by surface composite oxide film stabilization treatment, improves the surface's anti-adhesive wear ability and thermal stability, reduces spark duration, and makes the material more suitable for explosion-proof tools and components in flammable and explosive environments. Attached Figure Description
[0032] Figure 1 This is a schematic diagram of the alloy microstructure of the present invention;
[0033] Figure 2 This is a schematic diagram of the precipitated phase distribution of the present invention. Detailed Implementation
[0034] The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.
[0035] A high-hardness explosion-proof beryllium copper alloy and its preparation method, including the following preparation process:
[0036] All embodiments use the following general preparation process:
[0037] Smelting and casting: Weigh Cu, Be, Ni, Co, Cr, Ti, Zr, Si, Mg and rare earth RE raw materials according to the set mass percentage, and smelt them in a vacuum induction melting furnace under an inert atmosphere. Low-frequency electromagnetic stirring is carried out during the smelting process, followed by degassing, slag removal and casting into ingots.
[0038] Homogenization treatment: Place the ingot in a homogenization furnace and keep it at 860-890℃ for 3-5 hours.
[0039] Hot working: The homogenized ingot is heated to 790-825℃ for hot rolling, hot forging or hot extrusion, with the total deformation controlled at 60-80%.
[0040] Solution treatment: After heat treatment, the material is held at 805-825℃ for 1-1.5 hours and then rapidly quenched in water.
[0041] Cold deformation: Cold rolling, cold drawing or cold extrusion of the solution-treated material at a rate of 12-25%.
[0042] Graded aging: First, pre-aging at 310-325℃ for 1-1.5 hours, then peak aging at 438-450℃ for 1-1.2 hours.
[0043] Low-temperature stabilization treatment: Finally, a stabilization treatment is carried out at 230-255℃ for 0.5-1 hour to obtain the finished alloy.
[0044] Example 1
[0045] Please see Figure 1 and Figure 2 A high-hardness explosion-proof beryllium copper alloy and its preparation method, wherein the raw material composition by mass percentage is as follows:
[0046] The composition is: Be 2.08%, Ni 1.30%, Cr 0.34%, Ti 0.055%, Zr 0.050%, Si 0.11%, Mg 0.022%, Ce 0.010%, La 0.004%, with the balance being Cu and unavoidable impurities.
[0047] The preparation process is as follows:
[0048] The above raw materials were melted in a vacuum induction furnace at a temperature controlled at 1180-1210℃. After 15 minutes of low-frequency electromagnetic stirring, the mixture was cast into a φ120mm ingot. The ingot was homogenized by holding at 880℃ for 4 hours, followed by three passes of hot rolling. The final hot working temperature was controlled at around 800℃, with a total deformation of approximately 70%. After hot working, the ingot was solution-treated at 820℃ for 1 hour, water-quenched, and then subjected to 18% cold rolling deformation. It was then pre-aged at 320℃ for 1.5 hours and peak-aged at 445℃ for 1 hour, followed by stabilization treatment at 240℃ for 1 hour to obtain the finished product. The alloy obtained in this embodiment has a fine microstructure, uniform grains, and a continuous surface oxide film.
[0049] Example 2
[0050] Please see Figure 1 and Figure 2 A high-hardness explosion-proof beryllium copper alloy and its preparation method, wherein the raw material composition by mass percentage is as follows:
[0051] The composition is: Be 2.03%, Ni 1.34%, Co 0.76%, Cr 0.31%, Ti 0.050%, Zr 0.052%, Si 0.10%, Mg 0.020%, Ce 0.008%, La 0.004%, with the balance being Cu and unavoidable impurities.
[0052] The preparation process is as follows:
[0053] After the raw materials are melted, they are cast into ingots. The ingots are then homogenized by holding them at 870℃ for 3.5 hours. Subsequently, they are processed using alternating hot forging and hot rolling, with a total deformation of 75%. After hot working, they are solution-treated at 815℃ for 1.2 hours and then rapidly water-quenched. After solution treatment, they undergo 20% cold drawing deformation, followed by pre-aging at 315℃ for 1 hour, peak aging at 440℃ for 1.2 hours, and finally stabilization treatment at 250℃ for 0.5 hours. In this example, the Ni and Co contents are slightly higher, resulting in a larger number of precipitated strengthening phases and a significant increase in material hardness.
[0054] Example 3
[0055] Please see Figure 1 and Figure 2 A high-hardness explosion-proof beryllium copper alloy and its preparation method, wherein the raw material composition by mass percentage is as follows:
[0056] The composition is: Be 2.10%, Ni 1.22%, Co 0.62%, Cr 0.38%, Ti 0.060%, Zr 0.055%, Si 0.13%, Mg 0.024%, Ce 0.012%, La 0.002%, with the balance being Cu and unavoidable impurities.
[0057] The preparation process is as follows:
[0058] After the raw materials were melted and cast in an inert atmosphere, they were homogenized by holding at 890℃ for 5 hours, followed by hot rolling with a total deformation of approximately 60%. The final hot working temperature was approximately 790℃, and the solution treatment temperature was 808℃. After holding at 808℃ for 1.5 hours, the material was water-quenched with a cold deformation of 15%. It was then pre-aged at 325℃ for 1 hour, followed by peak aging at 450℃ for 1 hour, and finally stabilized at 230℃ for 1 hour. This embodiment emphasizes grain refinement and grain boundary purification, resulting in more discontinuous surface sparks after material impact.
[0059] Example 4
[0060] Please see Figure 1 and Figure 2 A high-hardness explosion-proof beryllium copper alloy and its preparation method, wherein the raw material composition by mass percentage is as follows:
[0061] The composition is: Be 2.06%, Ni 1.28%, Co 0.68%, Cr 0.35%, Ti 0.058%, Zr 0.048%, Si 0.12%, Mg 0.018%, Ce 0.009%, La 0.005%, with the balance being Cu and unavoidable impurities.
[0062] The preparation process is as follows:
[0063] During smelting, a combination of low-frequency electromagnetic stirring and vacuum refining was used. After casting, the ingot was homogenized by holding it at 875℃ for 4 hours, followed by hot extrusion forming with a total deformation of approximately 80%. It was then solution-treated at 818℃ for 1 hour, followed by 25% cold rolling, pre-aging at 312℃ for 1.5 hours, peak aging at 442℃ for 1 hour, and finally stabilization treatment at 245℃ for 0.5 hours. The resulting surface oxide film is relatively dense and exhibits good resistance to adhesive wear.
[0064] Example 5
[0065] Please see Figure 1 and Figure 2 A high-hardness explosion-proof beryllium copper alloy and its preparation method, wherein the raw materials are as follows by mass percentage:
[0066] The composition is: Be 2.04%, Ni 1.38%, Co 0.74%, Cr 0.30%, Ti 0.045%, Zr 0.046%, Si 0.095%, Mg 0.019%, Ce 0.006%, La 0.006%, with the balance being Cu and unavoidable impurities.
[0067] The preparation process is as follows:
[0068] After homogenization treatment at 860℃ for 3 hours, the ingot was processed by a combination of hot rolling and hot forging, with a total deformation of approximately 65%. The solution temperature was 810℃, followed by water quenching after 1.2 hours, resulting in a cold deformation of 12%. It was then pre-aged at 310℃ for 1 hour, peak-aged at 438℃ for 1.2 hours, and finally stabilized at 255℃ for 1 hour. In this embodiment, the cold deformation was minimal, the material's electrical conductivity was well maintained, and the hardness remained at a high level.
[0069] Example 6
[0070] Please see Figure 1 and Figure 2 A high-hardness explosion-proof beryllium copper alloy and its preparation method, wherein the raw material composition by mass percentage is as follows:
[0071] The composition is: Be 2.12%, Ni 1.25%, Co 0.80%, Cr 0.42%, Ti 0.065%, Zr 0.058%, Si 0.118%, Mg 0.023%, Ce 0.007%, La 0.005%, with the balance being Cu and unavoidable impurities.
[0072] The preparation process is as follows:
[0073] After the raw materials are smelted, casting is completed at approximately 1185℃. The ingot is then homogenized by holding at 885℃ for 4.5 hours, followed by hot rolling at 820℃ with a total deformation of approximately 78%. Solution treatment is then performed at 822℃, followed by rapid water quenching after 1 hour, resulting in a cold deformation of 22%. Subsequently, pre-aging at 323℃ for 1.5 hours, peak aging at 448℃ for 1 hour, and finally stabilization treatment at 235℃ for 1 hour are carried out. This embodiment represents a high-strength configuration with the highest hardness, suitable for high-impact explosion-proof components.
[0074] Performance testing:
[0075] 1. Testing method:
[0076] The alloy samples obtained in the above embodiments were subjected to the following tests:
[0077] Microhardness: Vickers hardness test was performed according to GB / T4340.1, with a load of 0.5 kg, and the average value of 5 points was taken;
[0078] Tensile properties: Prepare standard tensile specimens according to GB / T228.1, and test tensile strength, yield strength and elongation;
[0079] Conductivity: Measured using an eddy current conductivity meter, results are expressed as %IACS;
[0080] Impact performance: The room temperature impact absorption energy was tested using standard notched impact specimens.
[0081] Friction spark test: A comparative friction spark test was conducted under the same load and rotation speed conditions to record whether a continuous spark band appeared and the duration of the spark.
[0082] 2. The test results are shown in Table 1 below.
[0083] Table 1 Test Results
[0084]
[0085] 3. Comparative Explanation
[0086] The test results show that all six examples exhibit high hardness and good impact performance. Among them, Examples 2, 4 and 6 have better overall performance. In particular, no continuous spark band appeared in the friction spark test, indicating that the present invention can maintain good explosion-proof characteristics under high hardness conditions after multi-element micro-alloying, graded aging and surface stabilization treatment.
[0087] Compared with single-strength beryllium copper, the sample of the present invention showed an increase in hardness without a significant decrease in elongation and impact absorption energy, indicating that the microstructure design of the present invention has a good overall balance.
[0088] Working principle:
[0089] This invention uses copper as a base and constructs a multi-element microalloying system by adding appropriate amounts of beryllium, nickel, cobalt, chromium, titanium, zirconium, silicon, magnesium and rare earth elements. Among them, beryllium, nickel and cobalt together form the main precipitation strengthening basis, chromium, titanium and zirconium are used to inhibit grain coarsening and improve microstructure stability, and silicon, magnesium and rare earth elements are used to purify grain boundaries and improve the continuity of surface oxide film. This composition design enables the alloy to obtain high hardness while avoiding the problems of embrittlement and increased spark sensitivity caused by simple strengthening.
[0090] After homogenization, hot working, solution treatment and cold deformation, the internal defects, segregation and coarse dendrite structure of the alloy are significantly weakened, the dislocation density is significantly increased, providing a large number of nucleation sites for subsequent precipitation. Then, through staged aging treatment, the precursor clusters are formed first, and then further transformed into fine and dispersed precipitates, thereby constructing high-density strengthening points in the grains, while controlling the formation of continuous brittle phases at the grain boundaries. This microstructure design achieves a simultaneous balance of high hardness, good toughness and impact stability.
[0091] In the final low-temperature stabilization treatment, a relatively dense composite oxide film can be formed on the alloy surface. This film is rich in silicon, magnesium, and rare earth-related oxide components, and it bonds firmly to the substrate. This reduces local adhesion and heat concentration effects during frictional contact. When the material operates under impact, friction, or shock conditions, the surface is less prone to forming continuous high-temperature spark chains, thus exhibiting good explosion-proof safety characteristics. Therefore, this invention achieves a balance between high hardness and low spark sensitivity through the synergistic effect of composition design, microstructure control, and surface stabilization.
[0092] It will be apparent to those skilled in the art that the present invention is not limited to the details of the exemplary embodiments described above, and that the invention can be implemented in other specific forms without departing from its spirit or essential characteristics. Therefore, the embodiments should be considered in all respects as exemplary and non-limiting, and the scope of the invention is defined by the appended claims rather than the foregoing description. Thus, all variations falling within the meaning and scope of equivalents of the claims are intended to be included within the present invention. No reference numerals in the claims should be construed as limiting the scope of the claims.
Claims
1. A high-hardness explosion-proof beryllium copper alloy, characterized in that: The alloy comprises the following components by mass percentage: Be 2.00-2.12%, Ni 1.18-1.38%, Co 0.60-0.82%, Cr 0.28-0.42%, Ti 0.045-0.065%, Zr 0.045-0.058%, Si 0.09-0.13%, Mg 0.018-0.028%, rare earth RE 0.008-0.015%, balance Cu and unavoidable impurities; After solution treatment, cold deformation and graded aging, the average size of the matrix grains is 2-10 μm, the average grain size of the precipitates is 5-40 nm, and the length of the continuous brittle phase at the grain boundaries is no more than 20%, so as to form an explosion-proof structure with high hardness, low spark sensitivity and impact resistance.
2. The high-hardness explosion-proof beryllium copper alloy according to claim 1, characterized in that: The rare earth RE is one or a combination of Ce and La, and the total content of Ce and La is 0.008-0.015%, wherein the mass ratio of Ce to La is 1:3-3:
1. The rare earth RE is used to purify grain boundary inclusions, inhibit the loosening of oxide film and promote the formation of a continuous and dense composite passivation layer on the surface, thereby reducing the probability of the alloy igniting under friction or collision conditions.
3. The high-hardness explosion-proof beryllium copper alloy according to claim 1, characterized in that: The Ni, Co, and Be together form a composite precipitation strengthening system during the aging process. The Ni-Be precipitate is the main strengthening phase, Co is used to stabilize the size and distribution of the precipitate, Cr, Ti, and Zr together inhibit abnormal grain growth and refine the grain boundary structure, and Si and Mg are used to improve the density and adhesion stability of the surface oxide film, so as to maintain impact toughness while increasing hardness.
4. The high-hardness explosion-proof beryllium copper alloy according to claim 1, characterized in that: After treatment, the alloy forms a composite dense oxide film with a thickness of 50-300 nm on its surface. The composite dense oxide film is enriched with Si, Mg and rare earth RE elements and is firmly bonded to the substrate. The composite dense oxide film is used to improve the surface's resistance to adhesive wear, reduce the local frictional heat concentration effect, and suppress the generation of continuous spark chains under impact conditions.
5. The high-hardness explosion-proof beryllium copper alloy according to claim 1, characterized in that: The microstructure of the alloy satisfies the following: nanoscale precursor clusters and dispersed precipitates are uniformly distributed along the grain, and only intermittently distributed refined grain boundary phases are formed at the grain boundaries; the Vickers hardness of the alloy is 350-430 HV, and it still maintains a low hardness decay rate under repeated impact loads, so as to achieve a synergistic balance between high hardness and explosion-proof stability.
6. A method for preparing a high-hardness explosion-proof beryllium copper alloy, applicable to the high-hardness explosion-proof beryllium copper alloy according to any one of claims 1-5, characterized in that: The preparation method includes the following steps: S1. Weigh the raw materials according to the mass percentage, melt them under a vacuum or inert protective atmosphere, and then degas and remove slag before casting them into ingots. S2. Homogenize the ingot at 860-900℃ for 2-5 hours; S3. The homogenized ingot is hot-worked at 780-830℃, with a total deformation of 60-80%; S4. After hot working, the material is solution treated at 800-830℃ for 1-2 hours and then rapidly water quenched. S5. Perform 10-25% cold deformation on the solution-treated material; S6. After cold deformation, the material is first pre-failed at 300-330℃ for 1-2 hours, and then peak aged at 430-460℃ for 1-1.5 hours. S7. Finally, a low-temperature stabilization treatment is performed at 230-260℃ for 0.5-1 hour to obtain a high-hardness explosion-proof beryllium copper alloy.
7. The method for preparing a high-hardness explosion-proof beryllium copper alloy according to claim 6, characterized in that: In step S1, a melting method combining low-frequency electromagnetic stirring and vacuum refining is adopted to make the melt composition distribution more uniform and reduce the oxygen content, sulfur content and non-metallic inclusion content. Among them, Be, Mg and rare earth RE are added in stages during the melting process to reduce volatilization loss and improve the solid solution efficiency of microalloying elements.
8. The method for preparing a high-hardness explosion-proof beryllium copper alloy according to claim 6, characterized in that: The hot working in step S3 is carried out in a cross deformation manner. The cross deformation manner includes alternating hot rolling and hot forging, or changing the deformation direction of adjacent passes during multi-pass hot rolling. High-density dislocations are introduced and the cast coarse dendrite structure is broken through the cross deformation manner, so as to provide uniform nucleation sites for subsequent precipitation strengthening.
9. The method for preparing a high-hardness explosion-proof beryllium copper alloy according to claim 6, characterized in that: The pre-aging in step S6 is used to form nanoscale precursor clusters in the matrix, and the peak aging is used to transform the precursor clusters into a dispersed precipitate phase. The pre-aging temperature is 310-325℃ and the time is 1-1.5 hours, and the peak aging temperature is 435-450℃ and the time is 1-1.2 hours, so as to control the size of the strengthening phase and avoid coarsening and embrittlement.
10. The method for preparing a high-hardness explosion-proof beryllium copper alloy according to claim 6, characterized in that: Step S7 is followed by a surface stabilization treatment, which involves holding the alloy at 180-230°C for 0.5-2 hours in an inert mixed atmosphere with an oxygen content of 1-8% to promote the formation of a composite dense oxide film rich in Si, Mg and rare earth RE on the alloy surface. The composite dense oxide film works synergistically with the substrate to improve the anti-friction ignition capability and surface wear resistance stability under explosion-proof conditions.