Method for preparing high-hardness wear-resistant tungsten-rhenium alloy rod reinforced by sigama phase

Abstract

The application discloses a preparation method of a high-hardness wear-resistant tungsten-rhenium alloy rod reinforced by a Sigama phase, and specifically comprises the following steps: ball-milling blue tungsten and ammonium rhenium to obtain uniformly mixed precursor powder; hydrogen-reducing the uniformly mixed precursor powder to obtain tungsten-rhenium pre-alloy powder; pressing and sintering the tungsten-rhenium alloy powder to obtain tungsten-rhenium alloy blank; performing free forging and breaking down treatment on the tungsten-rhenium alloy blank; performing heating and rotary forging treatment; and performing high-temperature annealing treatment.The application controls the content of rhenium in the alloy, the processing temperature and the annealing temperature strictly, so that the Sigama phase is precipitated in the annealing process, the hardness of the tungsten-rhenium alloy is increased, and the wear resistance of the tungsten-rhenium alloy is improved.

Description

Technical Field

[0001] This invention belongs to the field of powder metallurgy preparation technology, specifically relating to a method for preparing a high-hardness, wear-resistant tungsten-rhenium alloy rod reinforced with Sigama phase. Background Technology

[0002] Tungsten, as the metal with the highest melting point, is widely used in aerospace, marine, electronic circuits, nuclear engineering, medical devices, and weaponry due to its excellent hardness, density, thermal conductivity, and low coefficient of thermal expansion. China possesses abundant tungsten resources and has become the world's largest exporter of tungsten raw materials. However, there is still a significant gap between domestically produced tungsten deep-processed products and those from abroad. Exports are mainly sintered billets and powders, and high-performance tungsten alloy deep-processed products still rely on imports.

[0003] Friction stir welding (FSW), a novel solid-state welding technology invented by the Welding Institute in the UK in 1991, boasts advantages such as energy saving, environmental friendliness, high quality, and high efficiency. Since its invention, it has received widespread attention and is considered the welding technology with the shortest time span from invention to industrial application in the history of global welding technology, hailed as the "second revolution in welding history" after laser welding. FSW is widely used in aerospace, shipbuilding, rail transportation, and automotive industries, and has become the preferred welding process for high-strength aluminum and magnesium alloys. Besides aluminum and magnesium alloys, FSW also has advantages in high-melting-point metals such as copper, steel, and titanium alloys, attracting increasing attention. However, during the welding of high-melting-point metals, the temperature of the friction stir head can reach 1000℃ due to intense friction. This temperature exceeds the recrystallization temperature of traditional iron-based materials. At such high temperatures, the strength of iron-based materials decreases rapidly, leading to a rapid reduction in material service life. Therefore, tungsten alloys, due to their high recrystallization temperature, have shown great potential in high-melting-point metal FSW.

[0004] Pure tungsten possesses high hardness and recrystallization temperature, but its inherent brittleness limits its application in friction stir welding. Improving the alloy composition is one of the most effective methods to reduce tungsten brittleness. Adding solid-solution elements or insoluble second phases to tungsten alloys can improve their microstructure and thus enhance their mechanical properties. Alloying pure tungsten with solid-solution elements is one of the most common methods to improve its mechanical properties. To overcome the low toughness and low ductile-brittle transition temperature of pure tungsten, one or more elements soluble in tungsten are added to improve the mechanical properties of tungsten alloys. Rhenium is the most common solid-solution element. Since the first report in 1995 that the addition of rhenium could improve the toughness of tungsten, extensive research has been dedicated to further exploring the mechanical properties of tungsten-rhenium alloys. Since metallic rhenium is a material without a ductile-brittle transition temperature, adding rhenium to tungsten can also lower its ductile-brittle transition temperature. In the tungsten-rhenium binary system, the solubility of rhenium in tungsten can reach 26% at room temperature. Within this solubility range, the mechanical properties gradually improve as the solid solubility of rhenium increases.

[0005] The solid solution strengthening effect of rhenium in tungsten is limited by its solubility. Introducing a second phase into tungsten-rhenium alloys can further improve their mechanical properties. The maximum solubility of rhenium in tungsten at room temperature is 26%. When the rhenium content exceeds this limit, the Sigma phase is formed. This phase is hard and brittle; while it can increase the hardness of the tungsten alloy, it also reduces its machinability. Therefore, the formation of the Sigma phase should be avoided during the forging and deformation process of tungsten-rhenium alloys. However, if the formation of the Sigma phase can be controlled to prevent its appearance during processing, and then allowed to occur after processing, the hardness of the tungsten-rhenium alloy can be improved while avoiding the decrease in machinability caused by the Sigma phase. It is worth noting that the solubility of rhenium in tungsten exceeds 32% above 1500°C; this characteristic can be utilized to prevent the precipitation of the Sigma phase during processing.

[0006] Traditional tungsten-rhenium alloys, due to their reliance on solid solution strengthening, have low hardness and poor wear resistance. To address these issues... Summary of the Invention

[0007] The technical problem to be solved by this invention is to address the shortcomings of the prior art by providing a method for preparing high-hardness, wear-resistant tungsten-rhenium alloy rods reinforced with the Sigama phase. This method strictly controls the composition ratio of the tungsten-rhenium alloy, the processing temperature, and the annealing temperature during the preparation of the tungsten-rhenium alloy rods to inhibit the formation of the Sigama phase during processing. Finally, annealing allows the tungsten-rhenium alloy rods to form the Sigama phase, thereby obtaining high-hardness, wear-resistant tungsten-rhenium alloy rods reinforced with the Sigama phase, thus solving the problem of decreased machinability caused by the formation of a second phase during forging.

[0008] To solve the above-mentioned technical problems, the technical solution adopted by the present invention is: a method for preparing a high-hardness, wear-resistant tungsten-rhenium alloy rod reinforced with Sigama phase, the preparation method specifically including the following steps:

[0009] S1) Preparation of tungsten-rhenium alloy precursor powder;

[0010] S2) The tungsten-rhenium alloy precursor powder of S1) is subjected to hydrogen reduction treatment to obtain tungsten-rhenium pre-alloy powder;

[0011] S3) The tungsten-rhenium pre-alloy powder obtained by cold isostatic pressing S2) is pressed and sintered in a hydrogen furnace to obtain tungsten-rhenium alloy billet;

[0012] S4) The tungsten-rhenium alloy billet obtained in S3) is heated and forged using an air hammer;

[0013] S5) The tungsten-rhenium alloy billet treated by S4) is subjected to heated rotary forging using rotary forging equipment;

[0014] S6) The tungsten-rhenium alloy billet after the spin forging process in S5) is subjected to high-temperature annealing in an annealing furnace to finally obtain a high-hardness, wear-resistant tungsten-rhenium alloy bar reinforced with Sigama phase.

[0015] Furthermore, the specific steps in S1) are as follows:

[0016] Using blue tungsten and ammonium perrhenate as raw materials, blue tungsten and ammonium perrhenate are weighed out according to the rhenium content accounting for 26% to 32% of the mass of tungsten and rhenium, respectively. The prepared powder is ball-milled using a ball mill to obtain a uniformly mixed tungsten-rhenium alloy precursor powder.

[0017] Furthermore, the purity of both the blue tungsten and ammonium rhenium is above 99.99%; the Fisher particle sizes of the blue tungsten and ammonium rhenium are 1μm~20μm and 1μm~70μm, respectively.

[0018] Furthermore, the specific process of hydrogen reduction treatment in S2) is as follows: first, hydrogen is reduced at a reduction temperature of 400℃~600℃ for 1h~3h; then, hydrogen is reduced at a reduction temperature of 900℃~1100℃ for 3h~6h.

[0019] Furthermore, in step S3), the density of the tungsten-rhenium alloy billet is between 88% and 93%, and the billet diameter should be a bar with a diameter of φ40mm to φ60mm.

[0020] Furthermore, the heating equipment for the billet forging process in S4) is a hydrogen furnace, with a heating temperature of 1650℃~1800℃, an initial heating and holding time of 0.5h~1h, an inter-pass heating time of 0.2h~0.3h, a 20%~30% reduction rate in the area of ​​the tungsten-rhenium alloy bar's circular surface per forging pass, and a diameter of φ18mm~φ22mm after air hammer forging.

[0021] Furthermore, the specific process of rotary forging in S5) is as follows: the heating temperature is 1550℃~1600℃, the initial heating and holding time is 0.5h~1h, the heating time between passes is 0.05h~0.2h, the area reduction rate of the tungsten rhenium alloy bar per pass of forging is 15%~25%, and the diameter of the tungsten rhenium alloy bar after rotary forging is φ10mm~φ16mm.

[0022] Furthermore, the heating equipment for the rotary forging process in S5) is a hydrogen furnace, a vacuum furnace, or an atmosphere furnace.

[0023] Furthermore, the annealing equipment in S6) is a hydrogen furnace, with an annealing temperature of 1000℃~1300℃ and a time of 1h~10h.

[0024] Compared with the prior art, the present invention has the following advantages:

[0025] 1. This invention sequentially prepares precursor powder by ball milling and mixing blue tungsten and ammonium rhenium oxide, obtains pre-alloyed powder by hydrogen reduction, obtains green billet by cold isostatic pressing, obtains tungsten-rhenium alloy billet by hydrogen furnace sintering, hot forging with air hammer, hot forging by rotary forging, and high-temperature annealing to prepare high-hardness, wear-resistant tungsten-rhenium alloy rods reinforced with Sigama phase. The powder composition, processing temperature, and heat treatment temperature are strictly controlled during the preparation process, thus obtaining high-hardness, wear-resistant tungsten-rhenium alloy rods reinforced with Sigama phase, solving the problem of low hardness and poor wear resistance in traditional tungsten-rhenium alloys that rely solely on solid solution strengthening.

[0026] 2. Compared with traditional processes for preparing tungsten-rhenium alloys, this invention creatively utilizes the Sigama phase as a reinforcing second phase to obtain high-hardness, wear-resistant tungsten-rhenium alloy rods. This invention leverages the characteristic that rhenium in tungsten will produce a Sigama phase beyond its solid solution limit, controlling the processing technology to avoid the precipitation of the Sigama phase during processing. Furthermore, it utilizes the high hardness of the Sigama phase, thus obtaining a tungsten-rhenium alloy reinforced with the Sigama phase without compromising processing performance. Attached Figure Description

[0027] Figure 1 This is a process flow diagram of the preparation method of a high-hardness, wear-resistant tungsten-rhenium alloy rod reinforced with Sigama phase according to the present invention.

[0028] Figure 2 The image shows the XRD pattern of the tungsten-rhenium pre-alloyed powder prepared in Example 1 of this invention.

[0029] Figure 3 Metallographic image of the microstructure of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in Example 1 of the present invention.

[0030] Figure 4 Scanning electron microscopy and composition diagrams of the microstructure of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in Example 1 of this invention.

[0031] Figure 5 This is a three-dimensional frictional morphology image of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in Example 1 of the present invention.

[0032] Figure 6 This is a physical image of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in Example 1 of the present invention.

[0033] Figure 7 The image shows the microstructure of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in Example 2 of this invention.

[0034] Figure 8 The image shows the three-dimensional morphology of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in Example 2 of this invention. Detailed Implementation

[0035] The technical solution of the present invention will be further described in detail below with reference to the accompanying drawings and embodiments.

[0036] like Figure 1 As shown, this invention discloses a method for preparing a high-hardness, wear-resistant tungsten-rhenium alloy rod reinforced with a Sigama phase. The method includes the following steps:

[0037] Step 1: Mix blue tungsten and ammonium rhenium in a certain proportion, and then use a ball mill to ball mill the prepared powder to obtain a uniformly mixed tungsten-rhenium alloy precursor powder.

[0038] Step 2: Use a hydrogen reduction furnace to reduce the tungsten-rhenium alloy precursor powder obtained in Step 1 with hydrogen to obtain tungsten-rhenium pre-alloy powder.

[0039] Step 3: The tungsten-rhenium mixed powder obtained in Step 2 is pressed by cold isostatic pressing and sintered in a hydrogen furnace to obtain tungsten-rhenium alloy billet;

[0040] Step 4: Use an air hammer to heat and forge the tungsten-rhenium alloy billet obtained in Step 3 to perform a billet-opening process.

[0041] Step 5: The tungsten-rhenium alloy billet after the air hammer blanking process in Step 4 is subjected to heating and rotary forging using a rotary forging equipment;

[0042] Step Six: The tungsten-rhenium alloy billet after the rotary forging process in Step Five is subjected to high-temperature annealing in an annealing furnace to finally obtain a high-hardness, wear-resistant tungsten-rhenium alloy.

[0043] In the above preparation method, the purity of both the blue tungsten and ammonium rhenium in step one is above 99.99%; the Fisher particle sizes of the blue tungsten and ammonium rhenium are 1μm-20μm and 1μm-70μm, respectively. High purity can reduce the adverse effects of impurity elements on the processing performance of tungsten-rhenium alloys; fine raw material particles can promote uniform mixing of powders and improve the alloying degree of the powder after hydrogen reduction.

[0044] In the above preparation method, the rhenium content in step one is between 26% and 32% of the mass of tungsten and rhenium. A high rhenium content is beneficial for the formation of the Sigama phase during the subsequent high-temperature annealing process. Typically, the rhenium content is between 26% and 30%.

[0045] In the above preparation method, no rhenium elemental phase appears in the tungsten-rhenium alloy powder after hydrogen reduction in step two; the hydrogen reduction temperature regime is 400℃~600℃ for 1h~3h + 900℃~1100℃ for 3h~6h. The selection of these parameters is beneficial for obtaining powders with a higher degree of alloying and avoids the formation of the Sigama phase during sintering and processing.

[0046] In the above preparation method, the density of the tungsten-rhenium alloy billet in step three is between 88% and 93%, and the billet diameter should be a bar with a diameter of φ40mm to φ60mm.

[0047] In the above preparation method, the heating equipment for the billet forging process in step four is a hydrogen furnace, with a heating temperature of 1650℃~1800℃, an initial heating holding time of 0.5h~1h, and an inter-pass heating time of 0.4h~0.6h. The area reduction rate of the tungsten-rhenium alloy bar per forging pass is 20%~30%, and the diameter of the tungsten-rhenium alloy bar after air hammer forging is φ18mm~φ22mm. The selection of these parameters helps to avoid the precipitation of the Sigama phase during processing, which reduces machinability.

[0048] In the above preparation method, the forging heating equipment in step five is a hydrogen furnace, with a heating temperature of 1550℃~1600℃, an initial heating holding time of 0.5h~1h, and an inter-pass heating time of 0.3h~0.6h. The area reduction rate of the tungsten-rhenium alloy bar per forging pass is 15%~25%, and the diameter of the forged tungsten-rhenium alloy bar is φ10mm~φ16mm. These parameter selections help to avoid the precipitation of the Sigama phase during processing, which reduces machinability.

[0049] In the above preparation method, the annealing equipment in step six can be a hydrogen furnace, a vacuum furnace, or an atmosphere furnace, with an annealing temperature of 1000℃~1300℃ and a time of 1h~10h. At this temperature and time, the solubility of the Sigama phase can be reduced, promoting the formation of the Sigama phase while avoiding recrystallization of the tungsten-rhenium alloy, ultimately yielding a high-hardness, high-wear-resistant tungsten-rhenium alloy rod.

[0050] Example 1

[0051] like Figure 1 As shown, this embodiment includes the following steps:

[0052] Step 1: Prepare tungsten powder and rhenium powder with a purity of 99.99% and Fisher particle sizes of 3μm and 50μm respectively at a mass fraction of 73% and 27%. Use a ball mill to ball mill the prepared powder to obtain a uniformly mixed tungsten-rhenium alloy precursor powder.

[0053] Step 2: Use a hydrogen reduction furnace to reduce the tungsten-rhenium alloy precursor powder obtained in Step 1 with hydrogen to obtain tungsten-rhenium pre-alloy powder. The hydrogen reduction parameters are 550℃ for 1 hour of hydrogen reduction + 1100℃ for 3 hours of hydrogen reduction.

[0054] Step 3: The tungsten-rhenium mixed powder obtained in Step 2 is pressed by cold isostatic pressing and sintered in a hydrogen furnace to obtain tungsten-rhenium alloy billet. The density of the sintered tungsten-rhenium alloy billet is 90%, and the billet is a bar with a diameter of φ50mm.

[0055] Step 4: The tungsten-rhenium alloy billet obtained in Step 3 is subjected to heating and forging treatment using an air hammer. The heating equipment for the forging treatment is a hydrogen furnace with a heating temperature of 1700℃. The initial heating and holding time is 0.5h, and the heating time between passes is 0.6h. The area reduction rate of the tungsten-rhenium alloy bar in each forging pass is 25%. The diameter of the tungsten-rhenium alloy bar after air hammer forging is φ18mm.

[0056] Step 5: The tungsten-rhenium alloy billet after the air hammer blanking process in Step 4 is subjected to hot rotary forging using a rotary forging equipment. The heating equipment for rotary forging is a hydrogen furnace with a heating temperature of 1600℃. The initial heating and holding time is 0.5h, and the heating time between passes is 0.4h. The area reduction rate of the tungsten-rhenium alloy bar per pass of forging is 20%. The diameter of the tungsten-rhenium alloy bar after rotary forging is φ14mm.

[0057] Step Six: The tungsten-rhenium alloy billet after the rotary forging process in Step Five is subjected to high-temperature annealing in an annealing furnace. The annealing equipment is an atmosphere furnace, the annealing temperature is 1300℃, and the time is 5h, finally obtaining a high-hardness and wear-resistant tungsten-rhenium alloy.

[0058] Figure 2 The image shows the XRD pattern of the tungsten-rhenium pre-alloyed powder prepared in this embodiment. It can be seen from the image that no elemental rhenium phase appeared after hydrogen reduction of the powder, indicating that the powder has a good degree of alloying.

[0059] Figure 3 The image shows the microstructure of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in this embodiment. It can be seen that the Sigama phase precipitates after annealing, which improves the hardness and wear resistance of the alloy.

[0060] Figure 4 The scanning electron microscope (SEM) and composition diagrams of the microstructure of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in this embodiment show that the rhenium content in the precipitate phase far exceeds the solid solubility limit of tungsten, confirming the precipitation of the Sigama phase.

[0061] Table 1 shows the hardness and wear rate of the W-25Re bars in this embodiment and the conventional W-25Re bars. The friction test was conducted using a circumferential ball-disc friction high-temperature testing machine. The friction test parameters were: temperature 1000℃, friction radius 3mm, rotation speed 560rpm, load 50N, and time 60min. As can be seen from the table, the hardness of the bars prepared in this embodiment is higher than that of the untreated W-25Re bars, and the wear resistance is also greatly improved.

[0062] Table 1. Hardness and wear rate of W-25Re bars in this embodiment and conventional W-25Re bars.

[0063]

[0064] Example 2

[0065] like Figure 1 As shown, this embodiment includes the following steps:

[0066] Step 1: Prepare tungsten powder and rhenium powder with a purity of 99.99% and Fisher particle sizes of 3μm and 50μm respectively at a mass fraction of 70% and 30%. Use a ball mill to ball mill the prepared powder to obtain a uniformly mixed tungsten-rhenium alloy precursor powder.

[0067] Step 2: Use a hydrogen reduction furnace to reduce the tungsten-rhenium alloy precursor powder obtained in Step 1 with hydrogen to obtain tungsten-rhenium pre-alloy powder. The hydrogen reduction parameters are 550℃ for 1 hour of hydrogen reduction + 1100℃ for 3 hours of hydrogen reduction.

[0068] Step 3: The tungsten-rhenium mixed powder obtained in Step 2 is pressed by cold isostatic pressing and sintered in a hydrogen furnace to obtain tungsten-rhenium alloy billet. The density of the sintered tungsten-rhenium alloy billet is 90%, and the billet is a bar with a diameter of φ50mm.

[0069] Step 4: The tungsten-rhenium alloy billet obtained in Step 3 is subjected to heating and forging treatment using an air hammer. The heating equipment for the forging treatment is a hydrogen furnace with a heating temperature of 1700℃. The initial heating and holding time is 0.5h, and the heating time between passes is 0.6h. The area reduction rate of the tungsten-rhenium alloy bar in each forging pass is 25%. The diameter of the tungsten-rhenium alloy bar after air hammer forging is φ18mm.

[0070] Step 5: The tungsten-rhenium alloy billet after the air hammer blanking process in Step 4 is subjected to hot rotary forging using a rotary forging equipment. The heating equipment for rotary forging is a hydrogen furnace with a heating temperature of 1600℃. The initial heating and holding time is 0.5h, and the heating time between passes is 0.4h. The area reduction rate of the tungsten-rhenium alloy bar per pass of forging is 20%. The diameter of the tungsten-rhenium alloy bar after rotary forging is φ14mm.

[0071] Step Six: The tungsten-rhenium alloy billet after the rotary forging process in Step Five is subjected to high-temperature annealing in an annealing furnace. The annealing equipment is an atmosphere furnace, the annealing temperature is 1300℃, and the time is 5h, finally obtaining a high-hardness and wear-resistant tungsten-rhenium alloy.

[0072] Figure 7 The image shows the microstructure of the high-hardness, wear-resistant tungsten-rhenium alloy rod prepared in this embodiment. It can be seen that the Sigama phase precipitates after annealing, which improves the hardness and wear resistance of the alloy.

[0073] Table 2 shows the hardness and wear rate of the W-25Re bars in this embodiment and the conventional W-25Re bars. The friction test was conducted using a circumferential ball-disc friction high-temperature testing machine. The friction test parameters were: temperature 1000℃, friction radius 3mm, rotation speed 560rpm, load 50N, and time 60min. As can be seen from the table, the hardness of the bars prepared in this embodiment is higher than that of the untreated W-25Re bars, and the wear resistance is also greatly improved.

[0074] Table 2. Hardness and wear rate of W-25Re bars in this embodiment and conventional W-25Re bars.

[0075]

[0076] The preparation method of the Sigama phase-reinforced high-hardness, wear-resistant tungsten-rhenium alloy rod provided in the embodiments of this application has been described in detail above. The descriptions of the above embodiments are only for the purpose of helping to understand the method and core ideas of this application; at the same time, for those skilled in the art, based on the ideas of this application, there will be changes in the specific implementation methods and application scope. Therefore, the content of this specification should not be construed as a limitation of this application.

[0077] Certain terms are used in the specification and claims to refer to specific components. Those skilled in the art will understand that hardware manufacturers may use different names to refer to the same component. This specification and claims do not distinguish components based on differences in name, but rather on differences in function. The terms "comprising" and "including" used throughout the specification and claims are open-ended and should be interpreted as "comprising / including but not limited to". "Approximately" means that within an acceptable margin of error, those skilled in the art can solve the technical problem and substantially achieve the technical effect within a certain margin of error. The following descriptions in the specification are preferred embodiments for carrying out this application; however, these descriptions are for the purpose of illustrating the general principles of this application and are not intended to limit the scope of this application. The scope of protection of this application shall be determined by the appended claims.

[0078] It should also be noted that the terms "comprising," "including," or any other variations thereof are intended to cover non-exclusive inclusion, such that a product or system comprising a list of elements includes not only those elements but also other elements not expressly listed, or elements inherent to such a product or system. Without further limitation, an element defined by the phrase "comprising one..." does not exclude the presence of other identical elements in the product or system that includes said element.

[0079] It should be understood that the term "and / or" used in this article is merely a description of the relationship between related objects, indicating that three relationships can exist. For example, A and / or B can represent: A existing alone, A and B existing simultaneously, and B existing alone. Additionally, the character " / " in this article generally indicates that the preceding and following related objects have an "or" relationship.

[0080] The foregoing description illustrates and describes several preferred embodiments of this application. However, as previously stated, it should be understood that this application is not limited to the forms disclosed herein and should not be construed as excluding other embodiments. It can be used in various other combinations, modifications, and environments, and can be altered within the scope of the application concept described herein through the foregoing teachings or techniques or knowledge in related fields. Any modifications and variations made by those skilled in the art that do not depart from the spirit and scope of this application should be within the protection scope of the appended claims.

Claims

1. A method for preparing a high-hardness, wear-resistant tungsten-rhenium alloy rod reinforced with Sigama phase, characterized in that, The preparation method specifically includes the following steps: S1) To prepare tungsten-rhenium alloy precursor powder, blue tungsten and ammonium rhenate are used as raw materials, and the rhenium content accounts for 26%~32% of the mass of tungsten and rhenium, respectively. S2) The tungsten-rhenium alloy precursor powder of S1) is subjected to hydrogen reduction treatment to obtain tungsten-rhenium pre-alloy powder; S3) The tungsten-rhenium pre-alloy powder obtained by cold isostatic pressing in S2) is pressed and sintered in a hydrogen furnace to obtain a tungsten-rhenium alloy billet; the density of the tungsten-rhenium alloy billet is between 88% and 93%, and the billet diameter should be a bar with a diameter of φ40mm to φ60mm; S4) The tungsten-rhenium alloy billet obtained in S3) is subjected to heating and forging using an air hammer. The heating equipment for the forging process is a hydrogen furnace, with a heating temperature of 1650℃~1800℃. The initial heating and holding time is 0.5h~1h, and the heating time between passes is 0.2h~0.3h. The area reduction rate of the tungsten-rhenium alloy bar's circular surface after each forging pass is 20%~30%. The diameter of the tungsten-rhenium alloy rods after air hammer forging is φ18mm~φ22mm; S5) The tungsten-rhenium alloy billet treated in S4) is subjected to hot rotary forging using rotary forging equipment. The specific process of rotary forging is as follows: the heating temperature is 1550℃~1600℃, the initial heating and holding time is 0.5h~1h, the heating time between passes is 0.05h~0.2h, the area reduction rate of the tungsten-rhenium alloy bar per pass of forging is 15%~25%, and the diameter of the tungsten-rhenium alloy bar after rotary forging is φ10mm~φ16mm. S6) The tungsten-rhenium alloy billet after the rotary forging treatment in S5) is subjected to high-temperature annealing in an annealing furnace. The annealing equipment is a hydrogen furnace, the annealing temperature is 1000℃~1300℃, and the time is 1h~10h. The composition ratio of tungsten-rhenium alloy, processing temperature and annealing temperature are strictly controlled to inhibit the formation of Sigama phase in tungsten-rhenium alloy during processing. Finally, the annealing process causes the tungsten-rhenium alloy rod to form Sigama phase, and finally obtains high-hardness wear-resistant tungsten-rhenium alloy rod strengthened by Sigama phase.

2. The preparation method according to claim 1, characterized in that, The purity of both the blue tungsten and ammonium rhenium is above 99.99%. The ferrochrome tungsten and ammonium rhenium have Fisher particle sizes of 1 μm to 20 μm and 1 μm to 70 μm, respectively.

3. The preparation method according to claim 1, characterized in that, The specific process of hydrogen reduction treatment in S2) is as follows: first, hydrogen is reduced at a reduction temperature of 400℃~600℃ for 1h~3h; then, hydrogen is reduced at a reduction temperature of 900℃~1100℃ for 3h~6h.

4. The preparation method according to claim 1, characterized in that, The heating equipment for rotary forging in S5) is a hydrogen furnace, a vacuum furnace, or an atmosphere furnace.

5. A tungsten-rhenium alloy rod, characterized in that, The tungsten-rhenium alloy rod is prepared by the preparation method described in any one of claims 1-4.

Images