Novel high-impact-resistance titanium alloy as well as preparation method and application of novel high-impact-resistance titanium alloy bar

Abstract

The invention belongs to the technical field of titanium alloy materials and bar machining of the titanium alloy materials, and particularly discloses a novel high-impact-resistance titanium alloy and a bar preparing method and application of the novel high-impact-resistance titanium alloy, and the novel high-impact-resistance titanium alloy is prepared from, by mass, 5.00%-6.70% of Al, 2.60%-4.60% of Mo, 0.80%-2.40% of Nb, 1.85%-3.50% of Sn, 1.80%-3.45% of Zr, 1.35%-2.70% of Cr, 0.060%-0.200% of O, 0.050%-0.150% of Si and the balance Ti and inevitable impurity elements. The sum of the mass percentages of the components is 100%. Through alloy component innovation and process collaborative optimization, the problem that strength, plasticity and toughness of novel titanium alloy are difficult to match under high-speed impact load is solved, and material support is provided for high performance and light weight in the fields of aerospace, national defense and military industry and the like.

Description

Technical Field

[0001] The present invention belongs to the technical field of titanium alloy materials and rod processing thereof, and particularly relates to a novel high-impact resistant titanium alloy and a preparation method and application of the rod thereof. Background Art

[0002] In many areas of national production, the performance of materials under high-speed impact loads directly impacts equipment effectiveness and safety. Typical scenarios, such as aircraft engine blades subjected to discrete source impacts, supersonic missiles penetrating military targets, and protective armor resisting ballistic impact, all place comprehensive demands on structural materials for high strength, high toughness, and lightweight design. Guided by the national energy conservation and consumption reduction strategy, structural weight reduction has become a key development direction in the aerospace, defense, and military industries, with the development of materials that combine novel and highly dynamic performance becoming a key breakthrough.

[0003] The traditional impact-resistant material is represented by 30CrMnSiNi2A steel, but the density of this material is as high as 7.8g / cm 3 , which significantly restricted the maneuverability and payload capacity of the equipment. With the development of titanium alloy technology, my country has introduced high specific strength titanium alloys into the field of high-speed penetration for the first time, and achieved the initial weight reduction goal through the application research of materials such as TC4 and TA15. Research on the application of titanium alloys such as TC4 and TA15 in high-speed penetration has been carried out successively. Our company has made breakthrough progress in the optimization of TA15 alloy. Through composition optimization and improved preparation process, and based on this technology, on July 17, 2015, we applied for a patent for "A high dynamic performance near-α-type titanium alloy and its preparation method". The application number is 201510421029.1, and it was authorized on October 2, 2018. The dynamic plastic strain of the TA15 titanium alloy reaches 0.26, the dynamic flow stress reaches 1560MPa, and the dynamic impact absorption energy reaches 405J / cm 3 , and its dynamic properties are significantly better than those of traditional TC4 alloy.

[0004] However, with the continuous upgrading of technical indicators of new equipment, materials are required to have the ability to resist impact deformation under high speed (penetration speed 850m / s) and high overload (30,000 to 50,000 times the acceleration of gravity) conditions. The existing material system faces multiple challenges: (1) the material density is required to be further reduced (the density is required to be less than 4.65g / cm 3 ) to improve the lightweight level of equipment; (2) require the material to be able to withstand high-speed strain conditions (10 3 S -1 ) has a better "strength-plasticity-toughness" match (dynamic flow stress at room temperature ≥1600MPa, dynamic plastic strain ≥0.30, dynamic impact absorption energy ≥440J / cm 3, Charpy impact ≥40J) to meet the service index requirements of new equipment; (3) In order to ensure the structural integrity of the equipment structure under high-speed penetration conditions, the material needs to have a high fracture toughness (K IC ≥90MPa·m 0.5 ); (4) The high-speed penetration time is in the microsecond level, which generates a large amount of heat that cannot be dissipated, causing a sharp rise in temperature and a softening effect. The material also needs to have good high-temperature performance (high-temperature strength and high-temperature dynamic performance). The current technology has the following bottlenecks: (1) The strength of traditional aluminum is insufficient and the density of steel is too high to meet the needs of new equipment; (2) Although the existing TA15 titanium alloy (ZL201510421029.1) has good dynamic performance, the key indicators still cannot meet the requirements; (3) High-strength titanium alloy TC18 (density 4.63g / cm 3 ), TB18(4.65g / cm 3 )、Ti55531(4.66g / cm 3 ) Due to the presence of high-density elements such as over 5wt% Mo and 3-5wt% Cr, the material density exceeds the specified limit, processing performance deteriorates, and Charpy impact and high-temperature performance are low. Existing material systems lack breakthroughs in the "strength-ductility-toughness" synergy mechanism and new alloy design theories, severely restricting the performance improvement of the next generation of equipment.

[0005] At the same time, the preparation process of high-impact resistant bars also faces the following technical difficulties that need to be solved urgently. For example, in the preparation process of electrodes for ingot smelting, due to the need to add a variety of intermediate alloy raw materials, the intermediate alloy forms vary greatly, including powder, granular and alloy chip states; in addition, during the assembly and welding of electrode blocks, if the heat input is large and the weld length is long, stress concentration is likely to occur, leading to cracking at the joints. In the subsequent smelting process, the weld position is prone to chip or block falling, thereby affecting the uniformity of the material composition.

[0006] Therefore, the development of new high-impact resistant titanium alloys with innovative composition systems and rod preparation processes has become a core technical problem that needs to be urgently solved in this field.

[0007] In view of this, this invention is proposed. Summary of the Invention

[0008] The purpose of the present invention is to overcome the shortcomings of the above-mentioned prior art and provide a new high-impact resistant titanium alloy and its rod preparation method and application, which are mainly used to solve the technical difficulties that structural materials in existing high-speed penetration scenarios cannot simultaneously meet the excellent "strength-plasticity-toughness" matching under light weight and high-speed strain conditions. Specifically, the density of traditional steel materials is too high, the strength of aluminum materials is insufficient, the key dynamic performance indicators of existing TA15 titanium alloys do not meet the new requirements of equipment upgrades, and high-strength titanium alloys containing high-density elements have excessive density and deteriorated processing performance, and low high-temperature performance. The present invention achieves comprehensive optimization of high impact resistance in high-speed penetration scenarios through innovative alloy composition design and rod preparation technology.

[0009] The purpose of the present invention is to solve the problem through the following technical solutions:

[0010] In a first aspect, the present invention provides a novel high-impact resistant titanium alloy, wherein the titanium alloy comprises the following elements, calculated by mass percentage:

[0011] Al: 5.00%~6.70%, Mo: 2.60%~4.60%, Nb: 0.80%~2.40%, Sn: 1.85%~3.50%, Zr: 1.80%~3.45%, Cr: 1.35%~2.70%, O: 0.060%~0.200%, Si: 0.050%~0.150%, the remainder is Ti and unavoidable impurity elements, C≤0.05%, N≤0.05%, H≤0.01%, and the sum of the mass percentages of the above components is 100%.

[0012] Preferably, the titanium alloy includes the following elements in percentage by mass:

[0013] Al: 5.80%~6.50%, Mo: 2.60%~3.70%, Nb: 1.60%~2.40%, Sn: 1.85%~3.00%, Zr: 1.80%~2.90%, Cr: 1.50%~2.10%, O: 0.100%~0.180%, Si: 0.060%~0.100%, the remainder is Ti and unavoidable impurity elements, C≤0.03%, N≤0.02%, H≤0.01%, and the sum of the mass percentages of the above components is 100%.

[0014] Furthermore, when preparing the titanium alloy, O and Si are used as key elements; the density of the titanium alloy is 4.58 g / cm 3 ~4.61g / cm 3 .

[0015] In a second aspect, the present invention provides a method for preparing the above-mentioned novel high-impact titanium alloy rod, the preparation method comprising the following steps:

[0016] Step 1: preparing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon as raw materials, and proportioning them according to the mass percentage, then fully mixing all the proportioned raw materials, and then pressing them into electrode blocks;

[0017] Step 2: placing the electrode block obtained in step 1 in an argon-filled protective environment, and welding the joints of the electrode block using a "breakpoint welding" process to form an electrode;

[0018] Step 3: subjecting the electrode obtained in step 2 to 2-3 vacuum consumable arc melting to form an alloy ingot;

[0019] Step 4: Forging the alloy ingot obtained in step 3 to form a bar;

[0020] Step 5: heat-treating the rod obtained in step 4, and then air-cooling to obtain the novel high-impact-resistant titanium alloy rod.

[0021] Specifically, the welding process of step 2 is as follows:

[0022] First, the electrode blocks required for a single electrode are placed in the plasma welding box, the box is evacuated to a vacuum degree of ≤5Pa, and then filled with argon to provide a stable inert gas environment for welding;

[0023] Next, adjust the position of the plasma welding gun so that it is in the center of the horizontal splicing gap to be welded, start welding along the horizontal splicing gap at a speed of 50mm / min to 150mm / min, control the moving distance to be 50mm to 150mm, and close the arc when the welding is 20mm to 50mm away from the cross splicing gap;

[0024] Afterwards, the plasma welding gun is moved at the set speed breakpoint to the farthest point at the lower end of the longitudinal splicing gap, and welding is carried out from bottom to top along the longitudinal splicing gap. The longitudinal welding distance is 60% of the longitudinal splicing gap length. After the longitudinal welding is completed, the welding gun is switched from longitudinal movement to transverse movement, and the arc is closed after welding another 20mm to 50mm along the transverse splicing gap.

[0025] Finally, the plasma welding gun is moved longitudinally to the transverse splicing gap at a set speed, and then transverse welding is performed along the transverse splicing gap at a set speed until the transverse gap is completely welded, thereby completing the breakpoint welding of a cross splicing gap; repeat the above steps to complete the welding of all cross splicing gaps of a single electrode.

[0026] Furthermore, in step 2, the parameters of the "breakpoint welding" process for welding the electrode block joints are set as follows: welding current is 200A to 500A, welding voltage is 40V to 90V, and argon flow rate is ≥0.5m3 / h.

[0027] Furthermore, in step 3, the parameters of the vacuum consumable arc melting are set as follows: the melting current is 12kA to 32kA, and the melting voltage is 20V to 50V.

[0028] Furthermore, in step 3, the alloy ingot is cylindrical in shape.

[0029] Furthermore, in step 4, the forging is divided into the following three stages, and the specific process is as follows:

[0030] Step 4.1, blank forging: After heating the alloy ingot at 100° C. to 250° C. above the phase transformation point, performing upsetting and drawing for 3 to 4 times, with the deformation amount of each fire controlled at 30% to 70%, to obtain a first blank;

[0031] Step 4.2, intermediate forging: After heating the first blank at 25°C to 90°C below the phase transformation point, perform upsetting and drawing for 3 to 4 times, with the deformation amount of each time controlled at 50% to 80%, to obtain a second blank;

[0032] Step 4.3, finished product forging: After heating the second blank at 45°C to 90°C below the phase transformation point, perform 2 to 4 fires of finished product forging, with the deformation amount of each fire controlled at 20% to 50%, to obtain a bar.

[0033] Furthermore, in step 4, the initial forging temperature of each stage of forging decreases with the increase in the number of fires, and air cooling is performed after each stage of forging.

[0034] Furthermore, the heat treatment adopts any of the following methods:

[0035] The first method is to place the rod obtained in step 4 in a temperature range of 700°C to 850°C for 4h to 8h annealing.

[0036] The second method is to first perform a solution treatment on the rod obtained in step 4 in a temperature range of 40°C to 80°C below the phase transformation point, and keep the temperature for 2h to 4h; then perform an aging treatment in a temperature range of 500°C to 650°C, and keep the temperature for 4h to 8h.

[0037] Furthermore, the properties of the titanium alloy bar prepared by the preparation method are as follows: at room temperature: Charpy impact ≥40J, fracture toughness ≥90MPa·m 0.5 , 10 3 S -1 Strain rate conditions: dynamic flow stress ≥1650MPa, dynamic plastic strain ≥0.32, dynamic impact absorption energy ≥560J / cm 3 ; Under high temperature conditions of 500℃: tensile strength ≥800MPa, 103 S -1 Strain rate conditions: dynamic flow stress ≥1258MPa, dynamic plastic strain ≥0.45, dynamic impact absorption energy ≥579J / cm 3 .

[0038] In a third aspect, the present invention provides a new type of high-impact-resistant titanium alloy rod prepared based on the above-mentioned preparation method, and the new type of high-impact-resistant titanium alloy is used in high-speed penetration scenarios.

[0039] The novel high impact resistant titanium alloy can be used for impact resistant parts of aero-engines, such as the manufacture of discrete source impact resistant structures for the leading edge of high pressure compressor blades. 3 S -1 Dynamic plastic strain at room temperature under strain rate ≥0.32, fracture toughness ≥90MPa·m 0.5 , so that the plastic deformation of the blade is controlled within 3mm when hit by a bird, avoiding fracture and failure. At the same time, due to the material density ≤4.61g / cm 3 , reducing the weight of the components, laying the foundation for improving the speed, endurance and load of aircraft; or for military purposes, such as for preparing gradient armor composite layers that are resistant to multiple impacts, with a dynamic rheological stress of ≥1650MPa, ensuring that the shell does not collapse and deform when resisting armor-piercing projectiles, and a dynamic impact absorption energy of ≥560J / cm 3 , Charpy impact ≥40J, can effectively dissipate more than 80% of the impact kinetic energy.

[0040] Compared with the prior art, the present invention has the following beneficial effects:

[0041] The novel high-impact titanium alloy provided by the present invention is a new titanium alloy composition designed based on first-principles calculations, according to the factors affecting the local shear deformation temperature rise during high-speed penetration and the influence of phase composition on dynamic performance. It has the following characteristics: 1) Nb, Sn, Mo, Cr, and Zr alloying elements are added to improve the heat capacity, melting point, and thermal strength of the titanium alloy to reduce the adiabatic temperature rise. At the same time, the ratio of each alloying element is strictly controlled to avoid the introduction of high-proportion high-density elements (such as Mo ≤ 4.6wt%, Cr ≤ 2.7wt%), so that the density of the titanium alloy is reduced to 4.58g / cm 3 ~4.61g / cm 3, which is significantly lower than traditional high-strength titanium alloys and meets the demand for lightweighting; 2) O element is used as the key element for material preparation (content 0.060% ~ 0.200%), and the content accuracy and distribution uniformity are strictly controlled. While ensuring the strength of the matrix, the material cracking sensitivity is reduced by regulating the balance between the oxygen solid solution strengthening effect and the grain boundary toughness, solving the contradiction that traditional titanium alloys are difficult to achieve both high strength and high toughness; 3) Si element is used as the key element for material preparation (content 0.050% ~ 0.150%), and the content accuracy and distribution uniformity are strictly controlled. The solid solution strengthening and precipitation strengthening effects are balanced, and the excessive precipitation of silicides is avoided while improving the thermal strength, which is especially suitable for the impact resistance requirements in high-speed penetration scenarios; 4) The present invention adopts appropriate welding current and voltage to control the input of welding heat and control the grain coarsening area of ​​the weld while ensuring the welding effect; argon protection is used in the welding process to avoid the weld being exposed to the oxidizing environment and to prevent the generation of brittle phases; the breakpoint is used Welding can effectively release welding stress, avoid cracks caused by stress concentration at the intersection of welds, improve welding quality and electrode reliability, and prevent chip or block falling at the weld position during subsequent smelting; 5) Through segmented forging above and below the phase transformation point (3 to 4 fires of rough forging above the phase transformation point to control the macrostructure, and multiple fires of fine forging below the phase transformation point to refine the grains), combined with the initial forging temperature control that decreases with the number of fires (air cooling after forging at each stage), the gradient optimization of the α and β dual-phase structure of the bar is achieved, which significantly improves the material's resistance to adiabatic shear and energy absorption efficiency during high-speed penetration; in addition, the optimized design of ingot casting and vacuum consumable arc melting parameters (current 12kA~32kA, voltage 20V~50V) ensures the uniformity of alloy composition and the density of the ingot, avoids the problem of processing performance degradation of traditional high-strength titanium alloys caused by high-density element segregation, and at the same time, the subsequent annealing treatment further eliminates the forging stress of the bar, stabilizes the microstructure, and ensures the uniformity of the final product performance.

[0042] In summary, the present invention has broken through the technical bottleneck of existing materials in terms of new and high impact resistance through the synergistic effect of composition design, process innovation and performance regulation. The density of the actually prepared titanium alloy has been tested to be only 4.58g / cm 3 ~4.61g / cm 3 ; Under room temperature conditions: Charpy impact ≥40J, fracture toughness ≥90MPa·m 0.5 , 10 3 S -1 Strain rate conditions: dynamic flow stress ≥1650MPa, dynamic plastic strain ≥0.32, dynamic impact absorption energy ≥560J / cm 3 ; Under high temperature conditions of 500℃: tensile strength ≥800MPa, 10 3 S -1Strain rate conditions: dynamic flow stress ≥1258MPa, dynamic plastic strain ≥0.45, dynamic impact absorption energy ≥579J / cm 3 It breaks through the performance bottleneck of existing TA15 alloy and traditional steel, achieves an excellent match of "high strength-high plasticity-high toughness", and can effectively resist deformation and fracture under high-speed impact loads, providing an ideal structural material for harsh scenarios such as high-speed penetration. BRIEF DESCRIPTION OF THE DRAWINGS

[0043] The accompanying drawings are incorporated in and constitute a part of this specification and, together with the description, serve to explain the principles of the invention.

[0044] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the following briefly introduces the drawings required for use in the embodiments or the description of the prior art. Obviously, for ordinary technicians in this field, other drawings can be obtained based on these drawings without any creative work.

[0045] Figure 1 This is a flow chart of the method for preparing the novel high impact resistant titanium alloy bar of the present invention;

[0046] Figure 2 This is a microstructure diagram of the titanium alloy rod prepared in Example 1 of the present invention;

[0047] Figure 3 This is a microstructure diagram of the titanium alloy rod prepared in Example 2 of the present invention;

[0048] Figure 4 This is a microstructure diagram of the titanium alloy rod prepared in Example 3 of the present invention;

[0049] Figure 5 This is a microstructure diagram of the titanium alloy rod prepared in Example 4 of the present invention;

[0050] Figure 6 This is the microstructure diagram of the titanium alloy rod prepared in Example 5 of the present invention. DETAILED DESCRIPTION

[0051] Exemplary embodiments will be described in detail herein, examples of which are illustrated in the accompanying drawings. In the following description, when referring to the drawings, identical numerals in different figures represent identical or similar elements unless otherwise indicated. The embodiments described in the following exemplary embodiments are not intended to represent all possible embodiments consistent with the present invention. Rather, they are merely examples of arrangements consistent with certain aspects of the present invention as detailed in the appended claims.

[0052] In order to enable those skilled in the art to better understand the technical solutions of the present invention, the present invention is described in further detail below with reference to the accompanying drawings and embodiments.

[0053] The new high impact resistant titanium alloy provided by the present invention is designed based on the following principles:

[0054] During the high-speed penetration of the target, the material will face severe tests and undergo severe plastic deformation. At the same time, the material body will heat up rapidly due to the rapid deformation. At this time, if the material has good plasticity and thermal strength, it can play a key role near the adiabatic shear band, enhance the deformation coordination ability, while maintaining high strength, and effectively delay the initiation and expansion of cracks. In the case of titanium alloys, the improvement of their thermal strength is usually closely related to the solid solution strengthening effect. In addition, increasing the melting point of titanium alloys helps to enhance the ability to suppress adiabatic temperature rise, while reducing the content of interstitial elements can enhance the toughness of titanium alloys.

[0055] The addition of alloying elements is an important means of modifying the properties of titanium alloys. These elements significantly influence physical properties such as bonding electron density, stacking fault energy, partial dislocation width, segregation energy, and axial ratio (c / a), thereby altering the macromechanical properties of titanium alloys. From the perspective of bonding electron density, it is generally believed that higher bonding electron density leads to greater lattice distortion and a stronger solid solution strengthening effect. Using first-principles calculations, researchers systematically investigated the effects of dozens of alloying elements on the relevant physical parameters of the α-Ti phase. Within the same period of the periodic table, with increasing valence electron number and decreasing atomic radius, lattice distortion and the degree of localized electron redistribution first increase and then decrease, resulting in a corresponding increase and then decrease in lattice distortion energy and electron work function. Notably, elements in groups 4d, 5d, and IVA have the highest electron density, resulting in greater crystal distortion and exhibiting a stronger solid solution strengthening effect, making them theoretically the most suitable alloying elements for high-strength titanium alloys. However, in practice, the higher atomic weight of 5d group elements increases alloy density; Si and Ge in group IVA easily induce the precipitation of hard and brittle phases; and elements such as Ru, Rh, and Ag in group 4d are expensive. Taking these factors into consideration, Zr, Nb, Mo, and Sn are more advantageous as alloying elements in high-impact titanium alloys from the perspective of solid solution strengthening.

[0056] The stacking fault energy is closely related to the dissociation of a dislocation into two Shockley partial dislocations and the twin fault formation energy. The lower the stacking fault energy, the greater the tendency for twin fault formation and the higher the alloy's plasticity. Elements such as Nb, Sn, Mo, Fe, and Cr can significantly reduce the stacking fault energy of the α-Ti phase.

[0057] The cross-slip and climb of partial dislocations are controlled by the stacking fault energy. The smaller the partial dislocation width, the greater the number of dislocations per unit volume, the higher the dislocation density, and the better the alloy's plasticity. Elements such as Cr, Mo, Al, V, Fe, Zr, and Sn can significantly reduce the partial dislocation width in the α-Ti phase.

[0058] Segregation energy refers to the change in interfacial energy caused by the segregation of alloying elements at stacking faults. The lower the segregation energy, the more stable the stacking faults, which facilitates plastic deformation of the alloy. Elements such as Nb, Sn, Mo, and Fe can significantly reduce the segregation energy of the α-Ti phase.

[0059] The axial ratio (c / a) significantly influences the twin shear behavior in HCP crystal structures. A lower axial ratio favors the initiation of prismatic and basal slip, thereby enhancing plasticity. Elements such as Nb, Cr, Mo, V, and Fe can reduce the c / a value of the α-Ti phase.

[0060] Generally speaking, the synergistic improvement of strength and plasticity can significantly improve the impact resistance of titanium alloys during high-speed penetration. Based on the effects of the various alloying elements on the performance of titanium alloys mentioned above, among the common titanium alloying elements, Nb, Sn, Mo, Fe, Cr, V and Zr elements all have the potential to improve the impact resistance of titanium alloys and are suitable as alloying elements for high-impact titanium alloys. However, the Fe element has a great tendency to segregate in titanium alloys and is very likely to cause serious metallurgical defects such as β spots, so it should be avoided as much as possible in practical applications. In summary, the present invention selects elements such as Nb, Sn, Mo, Cr and Zr as alloying elements for high-impact titanium alloys.

[0061] See also Figure 1 The present invention provides a novel method for preparing a high-impact titanium alloy rod, which specifically comprises the following steps:

[0062] Step 1: Prepare sponge titanium, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, sponge zirconium, titanium dioxide and aluminum silicon as raw materials, and mix them according to the mass percentage, then fully mix all the raw materials after mixing, and then press them into electrode blocks.

[0063] The element ratios in the electrode block, calculated by mass percentage, are as follows: Al: 5.00%-6.70%, Mo: 2.60%-4.60%, Nb: 0.80%-2.40%, Sn: 1.85%-3.50%, Zr: 1.80%-3.45%, Cr: 1.35%-2.70%, O: 0.060%-0.200%, Si: 0.050%-0.150%. The remainder is Ti and unavoidable impurities, with C ≤ 0.05%, N ≤ 0.05%, and H ≤ 0.01%. The sum of the above mass percentages is 100%. It should be noted that O and Si are key elements in the formulation, and their compositional accuracy and uniformity are controlled to ensure basic strength while improving toughness and thermal resistance and reducing cracking sensitivity.

[0064] Step 2: Place the electrode block obtained in step 1 in an argon-filled protective environment, and use a "breakpoint welding" process to weld the joints of the electrode block to form an electrode.

[0065] The parameters for welding the electrode block joints in the “breakpoint welding” process are as follows: welding current is 200A to 500A, welding voltage is 40V to 90V, and argon gas flow rate is ≥0.5m 3 / h.

[0066] Step 3: subjecting the electrode obtained in step 2 to 2-3 vacuum consumable arc melting to form an alloy ingot.

[0067] The alloy ingot is cylindrical in shape; the parameters of vacuum consumable arc melting are set as follows: the melting current is 12kA to 32kA, and the melting voltage is 20V to 50V.

[0068] Step 4: Forging the alloy ingot obtained in step 3 to make a rod.

[0069] Among them, forging is divided into the following three stages, the specific process is as follows:

[0070] Step 4.1, blank forging: After heating the alloy ingot at 100° C. to 250° C. above the phase transformation point, performing upsetting and drawing for 3 to 4 times, with the deformation amount of each fire controlled at 30% to 70%, to obtain a first blank;

[0071] Step 4.2, intermediate forging: After heating the first blank at 25°C to 90°C below the phase transformation point, perform upsetting and drawing for 3 to 4 times, with the deformation amount of each time controlled at 50% to 80%, to obtain a second blank;

[0072] Step 4.3, finished product forging: After heating the second blank at 45°C to 90°C below the phase transformation point, perform 2 to 4 fires of finished product forging, with the deformation amount of each fire controlled at 20% to 50%, to obtain a bar.

[0073] It should be noted that the initial forging temperature of each of the above stages decreases with the increase in the number of fires, and air cooling is performed after each stage of forging.

[0074] Step 5: heat-treating the rod obtained in step 4, and then air-cooling to obtain the novel high-impact-resistant titanium alloy rod.

[0075] Specifically, the heat treatment of the present invention adopts any of the following methods:

[0076] The first method is to place the rod obtained in step 4 in a temperature range of 700℃ to 850℃ for 4h to 8h annealing.

[0077] The second method is to first perform a solution treatment on the rod obtained in step 4 in a temperature range of 40°C to 80°C below the phase transformation point, and keep the temperature for 2h to 4h; then perform an aging treatment in a temperature range of 500°C to 650°C, and keep the temperature for 4h to 8h.

[0078] In order to further verify the efficacy of the present invention, the inventors conducted the following specific experiments:

[0079] Example 1

[0080] The novel high-impact titanium alloy bar prepared in this embodiment is designed with a composition based on mass percentage, specifically comprising 5.00% Al, 4.60% Mo, 0.80% Nb, 3.50% Sn, 2.10% Zr, 1.50% Cr, 0.200% O, and 0.050% Si, with the remainder being Ti and unavoidable impurity elements. Meanwhile, the impurity content is strictly controlled, requiring C ≤ 0.05%, N ≤ 0.05%, and H ≤ 0.01%. The detailed preparation process is as follows:

[0081] 1) mixing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon according to the above mass percentages, and pressing them into electrode blocks using a press and a mold;

[0082] 2) Using a vacuum plasma welding box, the electrode blocks obtained in step 1) were welded at the joints by “breakpoint welding” in an argon-filled environment to form electrodes. The welding current was 200A, the welding voltage was 40V, and the argon flow rate was 0.7m 3 / h;

[0083] 3) The electrode is subjected to three vacuum consumable arc melting processes to form an alloy ingot with a specification of Φ720 mm, with a melting current of 12 kA to 28 kA and a melting voltage of 20 V to 40 V;

[0084] 4) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to peeling, flaw detection, and riser sawing, and then samples were taken for chemical composition testing. The results are shown in Table 1 below:

[0085] Table 1 Chemical composition test results of alloy ingot of Example 1 (wt%)

[0086] Location Al Mo Nb Sn Zr Cr O Si C N H Ti head 5.06 4.58 0.82 3.48 2.09 1.50 0.200 0.050 0.02 0.01 0.01 margin middle 5.13 4.59 0.83 3.51 2.11 1.51 0.200 0.050 0.02 0.02 0.01 margin tail 5.12 4.57 0.81 3.50 2.12 1.51 0.201 0.050 0.02 0.01 0.01 margin

[0087] 5) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to three rounds of blank forging, with the forging method being upsetting and drawing, the heating temperatures being 200° C., 160° C., and 100° C. above the phase transformation point, respectively, and the deformation amount in each round being controlled at 30%, 45%, and 55%, respectively. After forging, the ingot was air-cooled to obtain a first blank;

[0088] 6) heating the first billet obtained in step 5) at 30° C., 45° C., and 60° C. below the phase transformation point, respectively, and then performing three intermediate forgings, wherein the forging method is upsetting and drawing, and the deformation amount of each fire is controlled at 50%, 60%, and 65%, respectively. After forging, the billet is air-cooled to obtain a second billet;

[0089] 7) The second billet obtained in step 6) is heated at 50° C. and 80° C. below the phase transformation point, respectively, and then subjected to two forging cycles, with the deformation of each cycle controlled at 40% and 30%, respectively, to produce a Φ380 mm bar;

[0090] 8) The rod obtained in step 7) is annealed at a temperature of 730° C. for 8 h (or first solution treated at 80° C. below the phase transformation point and kept warm for 4 h, and then aged at 500° C. and kept warm for 8 h), and air-cooled to obtain a Φ380 mm finished titanium alloy rod.

[0091] The internal structure, density and dynamic mechanical properties of the finished titanium alloy bar prepared in Example 1 were tested respectively. Figure 2 Table 2 shows the performance of the finished titanium alloy bar in Example 1 (dynamic performance at 10 3 S -1 Level strain rate test conditions):

[0092] Table 2 Performance test results of finished titanium alloy bars of Example 1

[0093]

[0094] Example 2

[0095] The novel high-impact titanium alloy bar prepared in this embodiment is designed with a composition by mass percentage, specifically comprising 5.80% Al, 4.10% Mo, 1.20% Nb, 3.00% Sn, 1.80% Zr, 2.70% Cr, 0.060% O, and 0.100% Si, with the remainder being Ti and unavoidable impurity elements. Meanwhile, the impurity content is strictly controlled, requiring C ≤ 0.05%, N ≤ 0.05%, and H ≤ 0.01%. The detailed preparation process is as follows:

[0096] 1) mixing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon according to the above mass percentages, and pressing them into electrode blocks using a press and a mold;

[0097] 2) Using a vacuum plasma welding box, the electrode blocks obtained in step 1) were welded at the joints by “breakpoint welding” in an argon-filled environment to form electrodes. The welding current was 350A, the welding voltage was 55V, and the argon flow rate was 0.6m 3 / h;

[0098] 3) The electrode is subjected to three vacuum consumable arc melting processes to form an alloy ingot with a specification of Φ720 mm, with a melting current of 16 kA to 32 kA and a melting voltage of 23 V to 42 V;

[0099] 4) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to peeling, flaw detection, and sawing of the riser, and then samples were taken for chemical composition testing. The results are shown in Table 3 below:

[0100] Table 3 Chemical composition test results of alloy ingots of Example 2 (wt%)

[0101] Location Al Mo Nb Sn Zr Cr O Si C N H Ti head 5.76 4.12 1.22 3.05 1.80 2.68 0.060 0.100 0.03 0.01 0.01 margin middle 5.81 4.09 1.19 3.02 1.81 2.71 0.060 0.101 0.02 0.02 0.01 margin tail 5.83 4.13 1.20 2.98 1.83 2.72 0.059 0.100 0.02 0.01 0.01 margin

[0102] 5) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to four rounds of blank forging, with the forging method being upsetting and drawing, the heating temperatures being 250° C., 190° C., 160° C., and 120° C. above the phase transformation point, respectively, and the deformation amount in each round being controlled at 50%, 45%, 55%, and 70%, respectively. After forging, the ingot was air-cooled to obtain a first blank;

[0103] 6) heating the first billet obtained in step 5) at 25° C., 35° C., and 50° C. below the phase transformation point, respectively, and then performing three intermediate forgings, wherein the forging method is upsetting and drawing, and the deformation amount of each fire is controlled at 60%, 65%, and 80%, respectively. After forging, the billet is air-cooled to obtain a second billet;

[0104] 7) The second billet obtained in step 6) is heated at 45° C. and 80° C. below the phase transformation point, respectively, and then subjected to two forging cycles, with the deformation of each cycle controlled at 40% and 20%, respectively, to produce a Φ380 mm bar;

[0105] 8) The rod obtained in step 7) is annealed at 810° C. for 4 h (or first solution treated at 70° C. below the phase transformation point and kept warm for 3 h, and then aged at 550° C. and kept warm for 6 h), and air-cooled to obtain a Φ380 mm finished titanium alloy rod.

[0106] The internal structure, density and dynamic mechanical properties of the finished titanium alloy bar prepared in Example 2 were tested respectively. Figure 3 The microstructure of the finished titanium alloy rod is shown in Table 4 below. The properties of the finished titanium alloy rod of Example 2 (dynamic properties at 10 3 S -1 Level strain rate test conditions):

[0107] Table 4 Performance test results of finished titanium alloy bars of Example 2

[0108]

[0109] Example 3

[0110] The novel high-impact titanium alloy bar prepared in this embodiment is designed with a composition based on mass percentage, specifically comprising 6.20% Al, 3.70% Mo, 1.60% Nb, 2.60% Sn, 2.90% Zr, 1.98% Cr, 0.100% O, and 0.150% Si, with the remainder being Ti and unavoidable impurity elements. Meanwhile, the impurity content is strictly controlled, requiring C ≤ 0.05%, N ≤ 0.05%, and H ≤ 0.01%. The detailed preparation process is as follows:

[0111] 1) mixing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon according to the above mass percentages, and pressing them into electrode blocks using a press and a mold;

[0112] 2) Using a vacuum plasma welding box, the electrode blocks obtained in step 1) were welded at the joints by “breakpoint welding” in an argon-filled environment to form electrodes. The welding current was 450A, the welding voltage was 70V, and the argon flow rate was 0.9m 3 / h;

[0113] 3) The electrode is subjected to three vacuum consumable arc melting processes to form an alloy ingot with a specification of Φ720 mm, with a melting current of 14 kA to 30 kA and a melting voltage of 22 V to 47 V;

[0114] 4) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to peeling, flaw detection, and riser sawing, and then samples were taken for chemical composition testing. The results are shown in Table 5 below:

[0115] Table 5 Chemical composition test results of alloy ingots of Example 3 (wt%)

[0116] Location Al Mo Nb Sn Zr Cr O Si C N H Ti head 6.17 3.72 1.57 2.62 2.88 1.98 0.100 0.149 0.02 0.01 0.01 margin middle 6.22 3.75 1.60 2.61 2.90 1.95 0.101 0.150 0.02 0.01 0.01 margin tail 6.22 3.70 1.62 2.58 2.93 1.93 0.100 0.150 0.02 0.01 0.01 margin

[0117] 5) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to four rounds of blank forging, with the forging method being upsetting and drawing, the heating temperatures being 180° C., 160° C., 120° C., and 100° C. above the phase transformation point, respectively, and the deformation amount in each round being controlled at 42%, 49%, 55%, and 60%, respectively. After forging, the ingot was air-cooled to obtain a first blank;

[0118] 6) heating the first billet obtained in step 5) at 30° C., 60° C., and 90° C. below the phase transformation point, respectively, and then performing three intermediate forgings, wherein the forging method is upsetting and drawing, and the deformation amount of each fire is controlled at 50%, 60%, and 70%, respectively. After forging, the billet is air-cooled to obtain a second billet;

[0119] 7) The second billet obtained in step 6) was heated at 45° C., 60° C., and 70° C. below the phase transformation point, and then forged into a finished product in three passes, with the deformation in each pass controlled at 45%, 30%, and 25%, respectively, to produce a Φ380 mm bar;

[0120] 8) The rod obtained in step 7) is annealed at a temperature of 770°C for 5 hours (or first solution treated at 60°C below the phase transformation point and kept warm for 3 hours, and then aged at 650°C and kept warm for 4 hours), and air-cooled to obtain a Φ380 mm finished titanium alloy rod.

[0121] The internal structure, density and dynamic mechanical properties of the finished titanium alloy bar prepared in Example 3 were tested respectively. Figure 4 The microstructure of the finished titanium alloy rod is shown in Table 6 below. The properties of the finished titanium alloy rod of Example 3 (dynamic properties at 10 3 S -1 Level strain rate test conditions):

[0122] Table 6 Performance test results of finished titanium alloy bars of Example 3

[0123]

[0124] Example 4

[0125] The novel high-impact titanium alloy bar prepared in this embodiment is designed with a composition based on mass percentage, specifically comprising 6.50% Al, 3.10% Mo, 2.00% Nb, 2.30% Sn, 2.65% Zr, 2.10% Cr, 0.150% O, and 0.060% Si, with the remainder being Ti and unavoidable impurities. Meanwhile, the impurity content is strictly controlled, requiring C ≤ 0.05%, N ≤ 0.05%, and H ≤ 0.01%. The detailed preparation process is as follows:

[0126] 1) mixing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon according to the above mass percentages, and pressing them into electrode blocks using a press and a mold;

[0127] 2) Using a vacuum plasma welding box, the electrode blocks obtained in step 1) were welded at the joints by “breakpoint welding” in an argon-filled environment to form electrodes. The welding current was 500A, the welding voltage was 90V, and the argon flow rate was 0.9m 3 / h;

[0128] 3) The electrode is subjected to two vacuum consumable arc melting processes to form an alloy ingot with a specification of Φ720 mm, with a melting current of 20 kA to 32 kA and a melting voltage of 28 V to 50 V;

[0129] 4) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to peeling, flaw detection, and riser sawing, and then samples were taken for chemical composition testing. The results are shown in Table 7 below:

[0130] Table 7 Chemical composition test results of alloy ingots of Example 4 (wt%)

[0131] Location Al Mo Nb Sn Zr Cr O Si C N H Ti head 6.47 3.11 1.98 2.28 2.67 2.07 0.151 0.061 0.03 0.02 0.01 margin middle 6.49 3.10 1.96 2.32 2.66 2.09 0.151 0.061 0.02 0.01 0.01 margin tail 6.51 3.08 2.03 2.32 2.63 2.11 0.150 0.060 0.02 0.01 0.01 margin

[0132] 5) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to three rounds of blank forging, with the forging method being upsetting and drawing, the heating temperatures being 180° C., 150° C., and 100° C. above the phase transformation point, respectively, and the deformation amount in each round being controlled at 52%, 58%, and 65%, respectively. After forging, the ingot was air-cooled to obtain a first blank;

[0133] 6) heating the first billet obtained in step 5) at 30° C., 45° C., and 60° C. below the phase transformation point, respectively, and then performing three intermediate forgings, wherein the forging method is upsetting and drawing, and the deformation amount of each fire is controlled at 55%, 60%, and 75%, respectively. After forging, the billet is air-cooled to obtain a second billet;

[0134] 7) The second billet obtained in step 6) was heated at 50° C., 60° C., 70° C., and 80° C. below the phase transformation point, and then subjected to four forging cycles, with the deformation of each cycle controlled at 40%, 30%, 30%, and 20%, respectively, to produce Φ380 mm bars;

[0135] 8) The rod obtained in step 7) is annealed at a temperature of 790° C. for 4 h (or first solution treated at 60° C. below the phase transformation point for 3 h, and then aged at 550° C. and kept warm for 6 h), and then air-cooled to obtain a Φ380 mm finished titanium alloy rod.

[0136] The internal structure, density and dynamic mechanical properties of the finished titanium alloy rod prepared in Example 4 were tested respectively; Table 8 below shows the properties of the finished titanium alloy rod in Example 4 (dynamic properties at 10 3 S -1 Level strain rate test conditions):

[0137] Table 8 Performance test results of finished titanium alloy bars of Example 4

[0138]

[0139] Example 5

[0140] The novel high-impact titanium alloy bar prepared in this embodiment is designed with a composition by mass percentage, specifically comprising 6.70% Al, 2.60% Mo, 2.40% Nb, 1.85% Sn, 3.45% Zr, 1.35% Cr, 0.180% O, and 0.080% Si, with the remainder being Ti and unavoidable impurities. Meanwhile, the impurity content is strictly controlled, requiring C ≤ 0.05%, N ≤ 0.05%, and H ≤ 0.01%. The detailed preparation process is as follows:

[0141] 1) mixing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon according to the above mass percentages, and pressing them into electrode blocks using a press and a mold;

[0142] 2) Using a vacuum plasma welding box, the electrode blocks obtained in step 1) are welded at the joints by “breakpoint welding” in an argon-filled environment to form electrodes. The welding current is 250A, the welding voltage is 45V, and the argon flow rate is 0.5m 3 / h;

[0143] 3) The electrode is subjected to two vacuum consumable arc melting processes to form an alloy ingot with a specification of Φ720 mm, with a melting current of 18kA to 28kA and a melting voltage of 27V to 47V;

[0144] 4) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to peeling, flaw detection, and riser sawing, and then samples were taken for chemical composition testing. The results are shown in Table 9 below:

[0145] Table 9 Chemical composition test results of alloy ingot of Example 5 (wt%)

[0146] Location Al Mo Nb Sn Zr Cr O Si C N H Ti head 6.73 2.56 2.35 1.82 3.42 1.37 0.180 0.079 0.03 0.02 0.01 margin middle 6.71 2.59 2.39 1.83 3.42 1.38 0.179 0.080 0.02 0.02 0.01 margin tail 6.66 2.63 2.42 1.85 3.46 1.36 0.179 0.080 0.02 0.01 0.01 margin

[0147] 5) The alloy ingot with a specification of Φ720 mm obtained in step 3) was subjected to four rounds of blank forging, with the forging method being upsetting and drawing, the heating temperatures being 210° C., 160° C., 130° C., and 100° C. above the phase transformation point, respectively, and the deformation amount in each round being controlled at 50%, 55%, 60%, and 65%, respectively. After forging, the ingot was air-cooled to obtain a first blank;

[0148] 6) heating the first billet obtained in step 5) at 20° C., 45° C., 60° C., and 90° C. below the phase transformation point, respectively, and performing four intermediate forgings, wherein the forging method is upsetting and drawing, and the deformation amount of each fire is controlled at 45%, 60%, 65%, and 75%, respectively. After forging, the billet is air-cooled to obtain a second billet;

[0149] 7) The second billet obtained in step 6) is heated at 50° C. and 90° C. below the phase transformation point, respectively, and then subjected to two forging cycles, with the deformation of each cycle controlled at 50%, 35%, 30%, and 20%, respectively, to produce a Φ380 mm bar;

[0150] 8) The rod obtained in step 7) is annealed at a temperature of 850° C. for 4 h (or first solution treated at 40° C. below the phase transformation point for 2 h, and then aged at 650° C. and kept warm for 4 h), and then air-cooled to obtain a Φ380 mm finished titanium alloy rod.

[0151] The internal structure, density and dynamic mechanical properties of the finished titanium alloy bar prepared in Example 5 were tested respectively; Table 10 below shows the properties of the finished titanium alloy bar in Example 5 (dynamic properties at 10 3 S -1 Level strain rate test conditions):

[0152] Table 10 Performance test results of finished titanium alloy bars of Example 5

[0153]

[0154] The new high impact resistant titanium alloy ingots prepared in Examples 1 to 5 of the present invention have good uniformity of composition, and the content of O and Si elements is precisely controlled; during the smelting process, the electrode strength is stable and no "block falling" phenomenon occurs. Figures 2 to 6The corresponding microstructure shows that the rod has a uniform structure and contains 45% to 60% equiaxed α phase content and no continuous β grain boundaries. In addition, the density and dynamic mechanical properties test results of the finished titanium alloy rods in Tables 2, 4, 6, 8 and 10 show that the density of the titanium alloy rod prepared by the present invention is 4.58 g / cm 3 ~4.61g / cm 3 ; Under room temperature conditions: Charpy impact ≥40J, fracture toughness ≥90MPa·m 0.5 , 10 3 S -1 Strain rate conditions: dynamic flow stress ≥1650MPa, dynamic plastic strain ≥0.32, dynamic impact absorption energy ≥560J / cm 3 ; Under high temperature conditions of 500℃: tensile strength ≥800MPa, 10 3 S -1 Strain rate conditions: dynamic flow stress ≥1258MPa, dynamic plastic strain ≥0.45, dynamic impact absorption energy ≥579J / cm 3 , fully meeting the requirements of new equipment for light weight and "strength-plasticity-toughness" under high-speed strain conditions.

[0155] The foregoing description is intended only to provide specific embodiments of the present invention, which will enable those skilled in the art to understand and implement the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the present invention.

[0156] It should be understood that the present invention is not limited to the above description and that various modifications and changes may be made without departing from the scope thereof. The scope of the present invention is limited only by the appended claims.

Claims

1. A new type of high impact resistant titanium alloy, characterized in that: The titanium alloy includes the following elements in percentage by mass: Al: 5.00%~6.70%, Mo: 2.60%~4.60%, Nb: 0.80%~2.40%, Sn: 1.85%~3.50%, Zr: 1.80%~3.45%, Cr: 1.35%~2.70%, O: 0.060%~0.200%, Si: 0.050%~0.150%, the remainder is Ti and unavoidable impurity elements, C≤0.05%, N≤0.05%, H≤0.01%, and the sum of the mass percentages of the above components is 100%.

2. The novel high impact resistant titanium alloy according to claim 1, characterized in that: The titanium alloy includes the following elements in percentage by mass: Al: 5.80%~6.50%, Mo: 2.60%~3.70%, Nb: 1.60%~2.40%, Sn: 1.85%~3.00%, Zr: 1.80%~2.90%, Cr: 1.50%~2.10%, O: 0.100%~0.180%, Si: 0.060%~0.100%, the remainder is Ti and unavoidable impurity elements, C≤0.03%, N≤0.02%, H≤0.01%, and the sum of the mass percentages of the above components is 100%.

3. The novel high impact resistant titanium alloy according to claim 1, characterized in that: When preparing the titanium alloy, O and Si are used as key elements; the density of the titanium alloy is 4.58 g / cm 3 ~4.61g / cm 3 .

4. A method for preparing a new high impact resistant titanium alloy rod according to any one of claims 1 to 3, characterized in that: The preparation method comprises the following steps: Step 1: preparing titanium sponge, aluminum-molybdenum alloy, niobium-titanium alloy, aluminum-chromium alloy, titanium-tin alloy, aluminum beans, zirconium sponge, titanium dioxide, and aluminum silicon as raw materials, and proportioning them according to the mass percentage, then fully mixing all the proportioned raw materials, and then pressing them into electrode blocks; Step 2: Place the electrode block obtained in step 1 in an argon-filled protective environment, and weld the joints of the electrode block using a "breakpoint welding" process to form an electrode; Step 3: subjecting the electrode obtained in step 2 to 2-3 vacuum consumable arc melting to form an alloy ingot; Step 4: Forging the alloy ingot obtained in step 3 to form a bar; Step 5: heat-treating the rod obtained in step 4, and then air-cooling to obtain the novel high-impact-resistant titanium alloy rod.

5. The method for preparing a new high impact resistant titanium alloy rod according to claim 4, characterized in that: In step 2, the parameters of the "breakpoint welding" process for welding the electrode block joints are set as follows: welding current is 200A to 500A, welding voltage is 40V to 90V, and argon flow rate is ≥0.5m 3 / h; In step 3, the parameters of the vacuum consumable arc melting are set as follows: the melting current is 12kA to 32kA, and the melting voltage is 20V to 50V.

6. The method for preparing a new high impact resistant titanium alloy rod according to claim 4, characterized in that: In step 3, the alloy ingot is cylindrical in shape.

7. The method for preparing a new high impact resistant titanium alloy rod according to claim 4, characterized in that: In step 4, the forging is divided into the following three stages, and the specific process is as follows: Step 4.1, blank forging: After heating the alloy ingot at 100° C. to 250° C. above the phase transformation point, performing upsetting and drawing for 3 to 4 times, with the deformation amount of each fire controlled at 30% to 70%, to obtain a first blank; Step 4.2, intermediate forging: After heating the first blank at 25°C to 90°C below the phase transformation point, perform upsetting and drawing for 3 to 4 times, with the deformation amount of each time controlled at 50% to 80%, to obtain a second blank; Step 4.3, finished product forging: After heating the second blank at 45°C to 90°C below the phase transformation point, perform 2 to 4 fires of finished product forging, with the deformation amount of each fire controlled at 20% to 50%, to obtain a bar.

8. The method for preparing a new high impact resistant titanium alloy rod according to claim 7, characterized in that: In step 4, the initial forging temperature of each stage of forging decreases with the increase of the number of fires, and air cooling is performed after each stage of forging.

9. The method for preparing a new high impact resistant titanium alloy rod according to claim 4, characterized in that: In step 5, the heat treatment is performed in any of the following ways: The first method is to place the rod obtained in step 4 in a temperature range of 700°C to 850°C for 4h to 8h annealing. The second method is to first perform a solution treatment on the rod obtained in step 4 in a temperature range of 40°C to 80°C below the phase transformation point, and keep the temperature for 2h to 4h; then perform an aging treatment in a temperature range of 500°C to 650°C, and keep the temperature for 4h to 8h.

10. A novel high impact resistant titanium alloy bar prepared by the preparation method according to any one of claims 4 to 9, characterized in that: The novel high impact resistant titanium alloy is used in high-speed penetration scenarios.

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