Lightweight heat-resistant titanium-based composite material, bar and preparation method thereof

Abstract

The invention provides a light heat-resistant titanium-based composite material, a bar and a preparation method of the light heat-resistant titanium-based composite material. The light heat-resistant titanium-based composite material comprises the following components in percentage by mass: 6.4-6.8% of Al; 1.5%-3.5% of Sn; 3.5%-5% of Zr; 0.2 to 0.6 percent of Mo; 1.5%-3% of Nb; 0.25 to 0.5 percent of Si; b: 0.3% to 0.6%; 0: less than or equal to 0.15%; c: < = 0.1%; fe: less than or equal to 0.035%; ti: the balance; wherein the content of Al, Sn and Zr meets the condition that (Al + Sn / 3 + Zr / 6) is less than or equal to 8.8. The small-specification heat-resistant titanium-based composite material bar which is low in density and ideal in indoor high-temperature comprehensive performance matching is prepared, the use economical efficiency of the material is greatly improved, and the material selection requirements for light weight and low cost of an existing high-performance advanced structure manufacturing technology are met.

Description

Technical Field

[0001] The present invention relates to the technical field of new material processing, and more particularly to a lightweight, heat-resistant titanium-based composite material, a rod and a preparation method thereof. Background Art

[0002] The rapid development of the aerospace industry has created an urgent need for low-cost, high-performance, lightweight, heat-resistant structural materials. High-temperature titanium alloys, titanium-based composites, Ti2AlNb, and TiAl / Ti3Al intermetallic compounds are currently the primary lightweight structural materials for hot-end components in high-performance advanced structural manufacturing operating at 600°C to 800°C. High-temperature titanium alloys, due to their intrinsic properties, rarely exceed a maximum service temperature of 600°C. Furthermore, as operating temperatures increase, the design of material composition systems becomes increasingly diversified and complex. This, in turn, leads to significant problems such as increased material density, increased difficulty in preparation, decreased yield, extended production cycles, rising manufacturing costs, decreased stability in microstructure and performance, and difficulty in coordinating and matching overall performance.

[0003] In order to meet the high-temperature service performance requirements of new structures for heat-resistant structural materials, the composition design of high-temperature titanium alloy materials used above 600℃ is becoming increasingly complex, with a density of usually 4.5g / cm 3 As high-temperature performance improves, density continues to increase. Currently, there are major issues such as low yield, high cost, insufficient high-temperature yield strength, and insufficient durability. Ti2AlNb and TiAl / Ti3Al intermetallic compounds offer excellent high-temperature performance and low density, but their application maturity is relatively low. Compared to traditional titanium alloys, their room-temperature plasticity is lower, making them more difficult to form and process. This results in high costs, low material utilization, and difficulty meeting the demand for mass-produced semi-finished bar products for large-scale components. Summary of the Invention

[0004] (1) Technical issues to be resolved

[0005] The technical problem to be solved by the present invention is that the existing high-temperature titanium-based materials have the problems of low material cost, high density, high cost, insufficient high-temperature yield strength and durability.

[0006] (2) Technical solution

[0007] To achieve the above object, the technical solution adopted by the present invention is:

[0008] In a first aspect, the present invention provides a lightweight, heat-resistant titanium-based composite material, comprising the following components by mass percentage: Al: 6.4-6.8%; Sn: 1.5-3.5%; Zr: 3.5-5%; Mo: 0.2-0.6%; Nb: 1.5-3%; Si: 0.25-0.5%; B: 0.3-0.6%; O: ≤0.15%; C: ≤0.1%; Fe: ≤0.035%; Ti: balance; wherein the contents of Al, Sn, and Zr elements satisfy (Al+Sn / 3+Zr / 6)≤8.8.

[0009] In a second aspect, the present invention also provides a rod-shaped material prepared from the lightweight and heat-resistant titanium-based composite material.

[0010] In a third aspect, the present invention further provides a method for preparing a rod, comprising the following steps:

[0011] S1. Determine the type and content of raw materials according to the ratio;

[0012] S2. Melting the raw materials using vacuum consumable arc melting technology to obtain a composite material ingot;

[0013] S3, performing multi-fire upsetting forging on the composite material ingot to obtain an intermediate forging blank;

[0014] S4, performing finish forging on the intermediate forging blank to obtain a bar of preset size;

[0015] S5. Heat-treating the bar material to obtain a bar material after the heat treatment is completed.

[0016] Preferably, the raw materials include zero-grade titanium sponge, high-purity aluminum particles, high-purity zirconium sponge, Ti-Sn master alloy, Al-Si master alloy, Al-Mo master alloy, Al-Nb master alloy, and titanium diboride powder.

[0017] Preferably, the composite material ingot is subjected to multi-fire upsetting forging to obtain an intermediate forging blank, comprising the following steps:

[0018] S31, using a fast forging machine to perform 1-2 heats of blanking deformation on the composite material ingot at 1150° C. to 1200° C., and air-cooling after forging to obtain a blank forged;

[0019] S32, after the forging is opened, the forging blank is heated to T by a step heating method. β ~T β +80℃ for 1 to 3 times of upsetting deformation, air cooling after forging to obtain the first-grade forging billet;

[0020] S33, reheating the first-level forging blank to T β -40℃~T β+60℃ for 2 to 6 times of upsetting deformation, followed by air cooling after forging to obtain the intermediate forging blank, wherein T β is the transition temperature of β phase of titanium matrix composites.

[0021] Preferably, in step S31, the composite material ingot is heated by a step preheating method, the preheating temperature is not less than 800°C, the upsetting and drawing ratio of each fire is not less than 3.2, the deformation speed is controlled at 20-50 mm / s, and the final forging temperature is not less than 900°C.

[0022] Preferably, in step S32, the step preheating temperature is not lower than 800°C. After preheating to the temperature, the forging billet is loaded into the furnace, heated with the furnace to the design temperature, taken out of the furnace and wrapped with insulation cotton, and then returned to the furnace for continued insulation for 120 to 360 minutes. The forging deformation speed is controlled at 10 to 50 mm / s, the iron drawing deformation per fire is 30% to 50%, the total forging ratio is greater than 6, and the final forging temperature is not lower than 850°C.

[0023] Preferably, in step S33, the step preheating temperature is not lower than 800°C. After preheating to the temperature, the forging billet is loaded into the furnace and heated with the furnace to the design temperature. It is then taken out of the furnace and wrapped with insulation cotton. It is then returned to the furnace and kept warm for 120 to 360 minutes. The forging deformation speed is controlled at 10 to 50 mm / s, the iron drawing deformation per fire is 20% to 45%, the total forging ratio is greater than 5.6, and the final forging temperature is not lower than 800°C.

[0024] Preferably, the precision forging of the intermediate forging blank to obtain a bar of preset size comprises the following steps: the intermediate forging blank is subjected to a T β -50℃~T β +100℃, 1 to 4 fires of fine forging are carried out, 2 to 6 deformations are carried out in each fire, the deformation amount of each pass is controlled at 5% to 30%, the final forging temperature is not lower than 800℃, and a fine forging blank is obtained. The fine forging blank is surface treated to obtain a bar of preset size.

[0025] Preferably, the heat treatment of the bar to obtain the bar after the heat treatment is completed includes the following steps: performing single-stage annealing or solution aging treatment or triple annealing heat treatment on the bar of the preset size to obtain the bar after the heat treatment is completed.

[0026] (3) Beneficial effects

[0027] The above technical solution of the present invention has at least the following advantages:

[0028] In response to the demand for lightweight, heat-resistant, high-performance structural materials in the 600℃~700℃ structural temperature range in aerospace and other fields, the present invention introduces a ceramic reinforcement phase into the matrix titanium alloy, rationally optimizes the ratio between the components, and uses a low-alloying method to prepare a small-scale heat-resistant titanium-based composite material rod with low density and ideal room-temperature comprehensive performance through reasonable thermal deformation and heat treatment processes. This greatly improves the economic efficiency of the material and meets the current lightweight and low-cost material selection requirements of high-performance advanced structural manufacturing technology. After deformation heat treatment, the rod prepared by the present invention has a density of <4.5g / cm 3 , the highest room temperature plasticity value> 8%, 650℃ yield strength> 510MPa, elongation> 12%, 650℃ / 200MPa lasting fracture time> 200h. The room and high temperature comprehensive performance match well. BRIEF DESCRIPTION OF THE DRAWINGS

[0029] In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the following briefly introduces the drawings required for use in the embodiments. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying any creative work.

[0030] Figure 1 It is a schematic flow chart of a method for preparing a rod provided in an embodiment of the present invention.

[0031] Figure 2 This is a photo of the rod provided in Example 1 of the present invention. DETAILED DESCRIPTION

[0032] In order to make the technical problems, technical solutions and beneficial effects to be solved by this application more clearly understood, the present application is further described in detail below in conjunction with the embodiments. It should be understood that the specific embodiments described herein are only used to explain this application and are not intended to limit this application.

[0033] It should be understood that in the various embodiments of the present application, the size of the serial numbers of the above-mentioned processes does not mean the order of execution. Some or all of the steps can be executed in parallel or sequentially. The execution order of each process should be determined by its function and internal logic, and should not constitute any limitation on the implementation process of the embodiments of the present application.

[0034] The terms used in the embodiments of the present application are for the purpose of describing specific embodiments only and are not intended to limit the present application. The singular forms "a", "an", "the" and "the" used in the embodiments of the present application and the appended claims are also intended to include plural forms unless the context clearly indicates otherwise.

[0035] The weights of the relevant components mentioned in the examples of this application may not only refer to the specific content of each component, but also represent the weight ratio between the components. Therefore, as long as the content of the relevant components is proportionally enlarged or reduced according to the examples of this application, it is within the scope disclosed in the examples of this application. Specifically, the mass described in the examples of this application may be a mass unit known in the chemical industry, such as μg, mg, g, kg, etc.

[0036] An embodiment of the present invention provides a lightweight, heat-resistant titanium-based composite material, comprising the following components, by mass percentage: Al: 6.4-6.8%; Sn: 1.5-3.5%; Zr: 3.5-5%; Mo: 0.2-0.6%; Nb: 1.5-3%; Si: 0.25-0.5%; B: 0.3-0.6%; O: ≤0.15%; C: ≤0.1%; Fe: ≤0.035%; Ti: balance; wherein the contents of Al, Sn, and Zr satisfy (Al + Sn / 3 + Zr / 6) ≤ 8.8. Controlling the contents of Al, Sn, and Zr to satisfy (Al + Sn / 3 + Zr / 6) ≤ 8.8 ensures the lightweight nature of the prepared material.

[0037] An embodiment of the present invention further provides a rod-shaped material prepared from a lightweight, heat-resistant titanium-based composite material.

[0038] An embodiment of the present invention further provides a method for preparing a rod, comprising the following steps:

[0039] S1. Determine the type and content of raw materials according to the ratio; specifically, first calculate the content of each element required for the composite material ingot to be smelted according to the nominal composition of the material, and then determine the type and content of each raw material for smelting based on the calculated element content.

[0040] S2. Vacuum consumable arc melting is used to melt the raw materials to obtain a composite material ingot. Specifically, the raw materials are weighed, mixed, pressed with electrodes, and then subjected to vacuum consumable arc melting to obtain a composite material ingot. This process is repeated three times to obtain a composite material ingot with uniform composition. To ensure the uniformity of the composite material ingot, single-electrode mixing and pressing are used. Because the addition of the reinforcing phase changes the fluidity of the titanium-based composite melt and internal stresses exist in large ingots, the electrodes are prone to cracking after electrode combination welding. Therefore, the electrode welding method and welding process can be optimized, or a single-electrode melting method can be used to melt the composite material ingot according to the melting equipment. Specifically, electron beam welding can be used to prepare strip electrode blocks, or appropriate welding process parameters can be selected to achieve welding of the strip electrode blocks. During melting, the strip electrode blocks are melted under vacuum using the high temperature generated by the arc discharge between the two electrodes of the strip electrode block and the crucible as the heat source. During melting, the consumable electrode continuously melts, while the ingot continuously solidifies and grows from bottom to top in the crystallizer. The composite material ingot obtained by the three smelting processes is subjected to riser treatment, ingot bottom sawing and skinning treatment to obtain a composite material ingot with uniform composition.

[0041] S3, performing multi-fire upsetting forging on the composite material ingot to obtain an intermediate forging blank;

[0042] S4, performing fine forging on the intermediate forging blank to obtain a bar of preset size;

[0043] S5. Heat-treating the bar material to obtain the bar material after the heat treatment is completed.

[0044] In one embodiment, the raw materials include zero-grade titanium sponge, high-purity aluminum particles, high-purity zirconium sponge, Ti-Sn master alloy, Al-Si master alloy, Al-Mo master alloy, Al-Nb master alloy, and titanium diboride powder.

[0045] In one embodiment, a composite material ingot is subjected to multi-fire upsetting forging to obtain an intermediate forging blank, comprising the following steps:

[0046] S31, using a fast forging machine to perform 1-2 heats of blanking deformation on the composite material ingot at 1150° C. to 1200° C., and air-cooling after forging to obtain a blank forged;

[0047] S32, after the forging is opened, the forging blank is heated to T by a step heating method. β ~T β +80℃ for 1 to 3 times of upsetting deformation, air cooling after forging to obtain the first-grade forging billet;

[0048] S33, reheat the first-level forging billet to T β -40℃~T β+60℃ for 2 to 6 times of upsetting deformation, air cooling after forging to obtain the intermediate forging billet, wherein T β is the transition temperature of the β phase of the titanium matrix composite material, T β It is 850℃~950℃.

[0049] In one embodiment, in step S31, the composite material ingot is heated by a step preheating method, the preheating temperature is not less than 800°C, the upsetting and drawing ratio of each fire is not less than 3.2, the deformation speed is controlled at 20-50 mm / s, and the final forging temperature is not less than 900°C.

[0050] In one embodiment, in step S32, the step preheating temperature is not lower than 800°C. After preheating to the temperature, the forging billet is loaded into the furnace and heated with the furnace to the design temperature. It is then wrapped with insulation cotton and returned to the furnace for continued insulation for 120 to 360 minutes. The forging deformation speed is controlled at 10 to 50 mm / s, the iron drawing deformation per fire is 30% to 50%, the total forging ratio is greater than 6, and the final forging temperature is not lower than 850°C.

[0051] In one embodiment, in step S33, the step preheating temperature is not lower than 800°C. After preheating to the temperature, the forging billet is loaded into the furnace and heated with the furnace to the design temperature. It is then wrapped with insulation cotton and returned to the furnace for continued insulation for 120 to 360 minutes. The forging deformation speed is controlled at 10 to 50 mm / s, the iron drawing deformation per fire is 20% to 45%, the total forging ratio is greater than 5.6, and the final forging temperature is not lower than 800°C.

[0052] In one embodiment, the intermediate forging blank is subjected to precision forging to obtain a bar of a preset size, comprising the following steps: β -50℃~T β Carry out 1 to 4 rounds of fine forging at +100℃, perform 2 to 6 deformation passes in each round, control the deformation amount in each pass at 5% to 30%, and the final forging temperature is not lower than 800℃ to obtain a fine forging blank, perform surface treatment on the fine forging blank, and obtain a bar of preset size.

[0053] In one embodiment, the bar is heat treated to obtain the bar after the heat treatment, comprising the following steps: performing single-stage annealing or solution aging treatment or triple annealing heat treatment on the bar of a preset size to obtain the bar after the heat treatment. Specifically, the bar of the preset size is subjected to single-stage annealing or solution aging treatment or triple annealing heat treatment at 600°C to 850°C for 4 to 8 hours or (T β -120℃~T β +80℃) / 0.5~2h / AC / QC / WQ+(600℃~800℃) / 4~8h / AC solution aging treatment or (T β -50℃~T β +80℃) / 0.5~2h / AC / QC / WQ+(T β-160℃~T β -70℃) / 1~2h / AC / QC / WQ+(600℃~800℃) / 4~8h / AC triple annealing heat treatment.

[0054] Specifically, the heat-resistant titanium-based composite material provided by the present invention is designed to have a long-term service temperature of 600°C to 650°C and a short-term service temperature of 700°C to 750°C. Currently, the heat-resistant structural materials available in this temperature range include high-temperature titanium alloys, intermetallic compounds, and high-temperature alloys. High-temperature alloys have high density and do not meet the weight reduction requirements in heat-resistant structures that require lightweight. Intermetallic compounds are difficult to prepare and process, and the low yield rate of industrial production leads to high material costs, which has shortcomings in economic use. Most high-temperature titanium alloys of 600°C to 650°C are evolved from the Ti-Al-Sn-Zr-Mo-Si system. Thermal strength is ensured by adding high-melting-point Nb, W, and Ta elements. The number of components is usually 7 to 10, and the density is between 4.5g / cm 3 ~4.7g / cm 3 It has certain processability and has a relatively ideal match in terms of density-processability-cost. However, in some heat-resistant structures with high requirements for high-temperature performance, there is still a problem of insufficient high-temperature performance, and its thermal strength decreases significantly after multiple high-temperature thermal cycles due to the influence of the intrinsic characteristics of the material. Due to the introduction of a ceramic phase with excellent thermal stability, the heat-resistant titanium-based composite material has outstanding load-bearing strengthening and dislocation strengthening effects at high temperatures, so that in the same temperature range, the titanium-based composite material can obtain ideal high-temperature thermal strength through a low-alloyed matrix component system. At the same time, due to the thermal stability of the enhanced phase, it can still maintain a high high-temperature performance after thermal cycling. Based on this design concept, in order to effectively control the cost of raw materials and reduce the density of materials, the present invention strictly controls the matrix alloy components and uses a high Nb design based on the traditional high-temperature titanium alloy system of Ti-Al-Sn-Zr-Mo-Si. The Nb element has weak β-stabilizing ability and has a certain solid solubility in both α and β phases. It is relatively evenly distributed and does not participate too much in the phase transformation process. Therefore, it has little effect on the size of each phase and mainly plays a role in solid solution strengthening. As the Nb content increases, T β The alloy's high-temperature tensile and yield strengths decrease, and the increase in yield strength is particularly significant. Therefore, the high-Nb design not only makes up for the problem of insufficient high-temperature strength of the matrix, but also avoids the problem of increased raw material costs and density caused by the simultaneous addition of high-melting-point alloying elements such as W and Ta. In addition, the high-Nb design combined with the strengthening effect of the reinforcing phase enables the composite material to have the same level of oxidation resistance and good durability / creep resistance as multi-component high-temperature titanium alloys. The addition of Nb elements also improves the overall deformation, processing and welding processability of the composite material, ensuring the manufacturing processability of titanium-based composite materials used as high-temperature structural materials.

[0055] Furthermore, due to the introduction of the reinforcement phase, the heat-resistant titanium-based composite material has a higher deformation resistance than conventional titanium alloys, a narrow hot working process window, poor forgeability of the blank during bar forging, prominent deformation cracking problems, and rapid crack propagation, making bar forming difficult and the yield rate seriously insufficient. At the same time, the hindering effect of the enhanced relative dislocation makes it easier for the matrix around the reinforcement phase to undergo dynamic recrystallization, resulting in large differences in the microstructure and properties at different positions of the bar, and the larger the bar size, the more prominent the inhomogeneity. Therefore, the traditional free forging process is no longer suitable for titanium-based composite materials. In response to the above problems, the present invention proposes for the first time a combined bar preparation process of free forging (multi-fire upsetting forging) + fine forging in titanium-based composite materials, utilizing the temperature rise effect during the fine forging process to reduce the surface temperature drop during the bar drawing process, reduce the deformation temperature gradient inside and outside the bar, improve the overall deformation uniformity, reduce deformation cracking, ensure the bar precision, improve the yield rate, and complete the bar microstructure and performance regulation through iterative optimization of the thermomechanical treatment process. Finally, a small-scale heat-resistant titanium-based composite material bar with low density and ideal room temperature comprehensive performance matching is prepared.

[0056] The present invention will be further described below with reference to the examples, but the present invention is not limited to the following examples.

[0057] Example 1

[0058] The heat-resistant titanium-based composite material in this embodiment is made of Al: 6.48%, Sn: 1.97%, Zr: 4.06%, Mo: 0.46%, Nb: 1.79%, Si: 0.34%, B: 0.49% and the balance Ti. The material density is 4.47g / cm 3 .

[0059] S1. Determine the types and contents of raw materials according to the proportions: First, perform a batching calculation based on the above ingredients to determine the content of each element required for a 1000kg ingot. Then, based on the calculated elemental contents, determine the types and contents of the raw materials used for smelting, including zero-grade titanium sponge, high-purity aluminum particles, high-purity zirconium sponge, Ti-Sn master alloy, Al-Si master alloy, Al-Mo master alloy, Al-Nb master alloy, and titanium diboride powder.

[0060] S2. Use vacuum consumable arc melting technology to melt raw materials and obtain composite material ingots: use the automatic mixing system equipped with vacuum consumable melting system combined with manual weighing to mix single electrode materials, then use 5000T hydraulic press to press electrodes, use vacuum plasma welding box (or electron beam welding equipment) to weld consumable electrodes, and perform three vacuum consumable melting after welding. During the melting process, the vacuum degree is maintained at 1.33Pa~5Pa. After the three ingots are peeled, risers are cut, and the bottom of the ingot is sawed, the ingot is obtained. Composite ingots.

[0061] S3. Perform multiple-fire upsetting and drawing forging on the composite material ingot to obtain an intermediate forging blank: Use a fast forging machine to perform two fires of upsetting and drawing deformation on the composite material ingot obtained in step S2 at 1150°C, with the total upsetting and drawing ratio of each fire being 7.2, the deformation speed being controlled at 20-50 mm / s, the final forging temperature being not less than 900°C, and air cooling after forging to obtain a forging blank after upsetting. Wrap the forging blank after upsetting with thermal insulation cotton and heat it to 1040-1100°C and perform three fires of drawing deformation, wherein the deformation temperature of the first fire is 1100°C, the deformation temperature of the second fire is 1040°C, and the deformation temperature of the third fire is 1100°C, the total upsetting and drawing ratio of each fire is 7.2, the deformation speed being controlled at 20-50 mm / s, the final forging temperature being not less than 850°C, and air cooling after forging to obtain a first-level forging blank. The first-level forging blank is wrapped with insulation cotton and heated to 1000℃~1060℃ for four rounds of iron drawing deformation, wherein the deformation temperature of the first fire is 1000℃, the deformation temperature of the second fire is 1060℃, the deformation temperature of the third fire is 1000℃, and the deformation temperature of the fourth fire is 1060℃. The total forging ratio of each fire is 7.2, the deformation speed is controlled at 10~50mm / s, the final forging temperature is not lower than 800℃, and it is air-cooled after forging to obtain an intermediate forging blank.

[0062] S4, the intermediate forging blank is finely forged to obtain a bar of preset size: the intermediate forging blank obtained in step S3 is finely forged at 1050℃~1120℃ for 2 times, with 4 deformation passes in each fire, and the deformation amount of each pass is controlled at 5%~30%. The final forging temperature is not less than 800℃. The bar after fine forging is subjected to surface treatment such as machining to obtain the bar of preset size. Figure 2 The small-sized finished bars shown are Ф60mm×L~4000mm.

[0063] S5. Heat treat the bar to obtain a bar after the heat treatment: the small-sized finished bar obtained in step S4 is subjected to a solution aging heat treatment of (1010°C-1035°C) for 1h / AC / WQ+700°C / 4h / AC and a triple annealing heat treatment of 1035°C / 1h / WQ+950°C / 1h / WQ+700°C / 4h / AC.

[0064] After heat treatment, small-sized heat-resistant titanium-based composite material rods with good room and high temperature performance were obtained. The properties of the rods after heat treatment are shown in Table 1 below.

[0065] Table 1 Mechanical properties of materials in Example 1

[0066]

[0067]

[0068] Durability test conditions: 650℃ / 200MPa

[0069] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions and improvements made within the spirit and principles of the present invention should be included in the scope of protection of the present invention.

Claims

1. A lightweight, heat-resistant titanium-based composite material, characterized in that: The following components are included by mass percentage: Al：6.4～6.8％； Sn: 1.5-3.5%; Zr：3.5～5％； Mo: 0.2~0.6%; Nb: 1.5-3%; Si: 0.25-0.5%; B：0.3～0.6％； O：≤0.15％； C：≤0.1％； Fe: ≤0.035%; Ti: margin; Among them, the contents of Al, Sn and Zr elements satisfy (Al+Sn / 3+Zr / 6)≤8.

8.

2. A rod, characterized in that: A rod-shaped material prepared from the lightweight, heat-resistant titanium-based composite material as claimed in claim 1.

3. A method for preparing a rod, characterized in that: The following steps are involved: S1. Determine the type and content of raw materials according to the ratio; S2. Melting the raw materials using vacuum consumable arc melting technology to obtain a composite material ingot; S3, performing multi-fire upsetting forging on the composite material ingot to obtain an intermediate forging blank; S4, performing finish forging on the intermediate forging blank to obtain a bar of preset size; S5. Heat-treating the bar material to obtain a bar material after the heat treatment is completed.

4. The method for preparing a rod according to claim 3, wherein: The raw materials include zero-grade sponge titanium, high-purity aluminum particles, high-purity sponge zirconium, Ti-Sn master alloy, Al-Si master alloy, Al-Mo master alloy, Al-Nb master alloy, and titanium diboride powder.

5. The method for preparing a rod according to claim 3, wherein: The composite material ingot is subjected to multi-fire upsetting forging to obtain an intermediate forging blank, comprising the following steps: S31, using a fast forging machine to perform 1-2 heats of blanking deformation on the composite material ingot at 1150° C. to 1200° C., and air-cooling after forging to obtain a blank forged; S32, after the forging is opened, the forging blank is heated to T by a step heating method. β ~T β +80℃ for 1 to 3 times of upsetting deformation, air cooling after forging to obtain the first-grade forging billet; S33, reheating the first-level forging blank to T β -40℃~T β +60℃ for 2 to 6 times of upsetting deformation, followed by air cooling after forging to obtain the intermediate forging blank, wherein T β is the transition temperature of β phase of titanium matrix composites.

6. The method for preparing a rod according to claim 5, wherein: In step S31, the composite material ingot is heated by a step preheating method, the preheating temperature is not less than 800°C, the upsetting and drawing ratio of each fire is not less than 3.2, the deformation speed is controlled at 20-50 mm / s, and the final forging temperature is not less than 900°C.

7. The method for preparing a rod according to claim 5, wherein: In step S32, the step preheating temperature is not lower than 800℃. After preheating to the temperature, the forging billet is loaded into the furnace and heated with the furnace to the design temperature. It is then wrapped with insulation cotton and returned to the furnace for continued insulation for 120 to 360 minutes. The forging deformation speed is controlled at 10 to 50 mm / s, the iron drawing deformation per fire is 30% to 50%, the total forging ratio is greater than 6, and the final forging temperature is not lower than 850℃.

8. The method for preparing a rod according to claim 5, wherein: In step S33, the step preheating temperature is not lower than 800℃. After preheating to the temperature, the forging billet is loaded into the furnace and heated with the furnace to the design temperature. It is then wrapped with insulation cotton and returned to the furnace for continued insulation for 120 to 360 minutes. The forging deformation speed is controlled at 10 to 50 mm / s, the iron drawing deformation per fire is 20% to 45%, the total forging ratio is greater than 5.6, and the final forging temperature is not lower than 800℃.

9. The method for preparing a rod according to claim 3, wherein: The process of fine forging the intermediate forging blank to obtain a bar of preset size comprises the following steps: The intermediate forging billet is at T β -50℃~T β +100℃, 1 to 4 fires of fine forging are carried out, 2 to 6 deformations are carried out in each fire, the deformation amount of each pass is controlled at 5% to 30%, the final forging temperature is not lower than 800℃, and a fine forging blank is obtained. The fine forging blank is surface treated to obtain a bar of preset size.

10. The method for preparing a rod according to claim 3, wherein: The bar material is subjected to heat treatment to obtain the bar material after the heat treatment is completed, comprising the following steps: The bar material of the preset size is subjected to single-stage annealing or solution aging treatment or triple annealing heat treatment, and the bar material is obtained after the heat treatment is completed.

Images