High-performance titanium-based part powder hot isostatic pressing preparation method based on low-cost near-spherical bimodal powder

Abstract

The application provides a high-performance titanium-based part powder hot isostatic pressing preparation method based on low-cost near-spherical bimodal powder. The preparation method uses a near-spherical bimodal particle size distribution titanium-based powder with good uniformity and high tap density as raw material, and combines powder hot isostatic pressing technology to prepare a high-performance low-cost titanium-based part, so as to meet the high-performance low-cost demand of complex structure and thin-walled titanium alloy parts in the fields of aerospace, weapon equipment and the like.

Description

High-performance titanium-based component powder hot isostatic pressing preparation method based on low-cost near-spherical bimodal powder Technical Field

[0001] This invention relates to the field of metal material preparation technology, specifically to a method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder. Background Technology

[0002] The rapid development of the aerospace industry in recent years has placed higher demands on the lightweight and high-performance of complex thin-walled cabins, air intakes, and other deep-cavity cylindrical components. These components not only exhibit complex deep-cavity, thin-walled structures but also face harsh service conditions such as high loads and high speeds in actual operation, thus requiring lightweight, high-strength, and high-temperature-resistant titanium alloys. However, due to the high activity, high melting point, and low thermal conductivity of titanium alloys, traditional casting and forging processes are difficult to use for manufacturing complex thin-walled deep-cavity cylindrical parts, resulting in long production cycles, high costs, and low material utilization. For example, in the Boeing 787 titanium alloy fuselage frame, approximately 83% of the material is wasted during machining. Near-net-shape hot isostatic pressing (NNS-HIP) technology combines the mold shell and core of complex parts and applies isostatic pressure to powder at high temperatures to achieve near-net-shape forming of the part, demonstrating unique advantages in the overall manufacturing of thin-walled complex titanium components. The NNS-HIP process is relatively simple, has a short production cycle, and high material utilization (it can be increased from 10%–20% of traditional processes to over 50%). Furthermore, the components produced have wide structural adaptability, high dimensional accuracy and surface quality, and uniform and fine microstructure, with overall performance reaching or even exceeding that of forgings. Therefore, in recent years, titanium alloy powder NNS-HIP technology has received widespread attention and research from scholars both domestically and internationally. However, its large-scale application still faces the challenge of low cost.

[0003] Powder raw materials, as the foundation of titanium alloy powder hot isostatic pressing (NNS-HIP) technology, are crucial in determining the cost and performance of manufactured parts. Currently, NNS-HIP technology primarily uses spherical powders with good flowability, high tap density, and low impurity content, prepared by inert gas atomization (GA) and plasma rotating electrode process (PREP). However, the high price of spherical titanium powder significantly increases the manufacturing cost of formed parts. To further reduce the cost of titanium powder, extensive cost reduction technology development and research have been conducted both domestically and internationally in recent years. These technologies generally utilize hydrogenated dehydrogenated (HDH) titanium powder, which has poor flowability but is inexpensive (approximately 250 RMB / kg), as raw material. Powder modification or shaping techniques such as plasma spheroidization, mechanical shaping, and high-temperature ball milling are used to improve its flowability to meet the requirements of hot isostatic pressing powders. However, although this method can reduce the cost of hot isostatic pressing powders and thus lower the production cost of titanium alloy powder NNS-HIP technology, the precision and mechanical properties of the formed parts still fall short of the requirements for high-end applications such as aerospace. Summary of the Invention

[0004] To overcome the shortcomings of the prior art, the main objective of this invention is to provide a method for preparing high-performance titanium-based parts by hot isostatic pressing of near-spherical bimodal powders based on low-cost near-spherical bimodal powders. This method uses near-spherical bimodal titanium-based powders with good uniformity and high tap density as raw materials, and combines them with hot isostatic pressing technology to prepare high-performance, low-cost titanium-based parts, thereby meeting the high-performance and low-cost requirements of aerospace, weaponry and other fields for thin-walled complex titanium alloy parts.

[0005] To achieve the above objectives, according to a first aspect of the present invention, a method for preparing high-performance titanium-based component powder by hot isostatic pressing based on low-cost near-spherical bimodal powder is provided.

[0006] The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder includes the following steps:

[0007] Nearly spherical titanium-based powder with a bimodal particle size distribution is obtained by using a particle size distribution method; wherein, the near-spherical titanium-based powder with a bimodal particle size distribution is near-spherical titanium powder with a bimodal particle size distribution or near-spherical titanium alloy powder with a bimodal particle size distribution;

[0008] The near-spherical titanium-based powder with a bimodal particle size distribution was loaded into the casing using a vibration method.

[0009] After vacuuming and sealing the encapsulation, hot isostatic pressing is performed to obtain a titanium-based component.

[0010] Furthermore, the near-spherical titanium-based powder with bimodal particle size distribution has a particle size of 30–150 μm, a flowability of 31–36 s / 50 g, and a tap density of 2.93–3.02 g / cm³. 3 .

[0011] Furthermore, the preparation of the near-spherical titanium-based powder with bimodal particle size distribution includes the following steps:

[0012] With two different medium particle sizes D 50 Near-spherical titanium powder is used as the raw material powder, or two different medium particle sizes D 50 Near-spherical titanium alloy powder is used as the raw material powder;

[0013] The raw material powder is placed in a suspension and stirred for a certain period of time to obtain a powder mixture slurry;

[0014] Under a protective atmosphere, the powder mixture slurry was degreased to obtain the near-spherical titanium-based powder with a bimodal particle size distribution.

[0015] Preferably, the titanium alloy powder includes, but is not limited to, Ti-6Al-4V alloy powder.

[0016] The differences between the various bimodal near-spherical titanium-based powders obtained in this invention lie in the different particle size ratios and mass ratios of the two raw material powders used. By testing the tap density of each bimodal powder, a modified Horsfield dense packing theory applicable to near-spherical powders is proposed to determine the range of particle size ratios and mass ratios of the two raw material powders in near-spherical bimodal distribution powders with high tap density. This guides the preparation of high-quality bimodal near-spherical titanium-based powders for hot isostatic pressing.

[0017] Furthermore, the raw material powder contains two different particle sizes D 50 The powders are referred to as fine powder and coarse powder, respectively. The fine powder has a particle size of 30-80 μm, and the coarse powder has a particle size of 80-150 μm.

[0018] Preferably, the medium particle size D of the fine powder and the coarse powder 50 The ratio is 0.414:1 to 0.360:1;

[0019] Preferably, the mass ratio of the fine powder to the coarse powder is 1:9 to 4:6.

[0020] Furthermore, the suspension is a mixture of polyethylene glycol 10000 and anhydrous ethanol, or a mixture of polyethylene glycol 10000 and deionized water.

[0021] Preferably, the mass of the polyethylene glycol 10000 accounts for 3-5% of the total mass of the raw material powder;

[0022] Preferably, the raw material powder accounts for 60-80% of the total mass of the powder mixture slurry.

[0023] Furthermore, the stirring speed is 300-600 r / min, and the stirring time is 2-8 h;

[0024] Preferably, the stirring is carried out under a high-purity argon protective atmosphere.

[0025] Furthermore, the degreasing temperature is 120–160°C, the heating rate is 0.5–3°C / min, and the degreasing time is 1–2 hours.

[0026] Preferably, the protective gas is high-purity argon.

[0027] Furthermore, before loading the near-spherical titanium-based powder with a bimodal particle size distribution, the packaging is subjected to ultrasonic cleaning and drying treatment in sequence;

[0028] Preferably, the encapsulation is vacuumed using an encapsulation thermal degassing system, with a vacuum degree ≤ 1.0 × 10⁻⁶. -3 Pa.

[0029] Furthermore, the hot isostatic pressing treatment is performed at a temperature of 750–1000℃, a pressure of 70–120 MPa, and a holding time of 3–5 hours.

[0030] Preferably, after the hot isostatic pressing process is completed, the pressure is released and the temperature is cooled to below 200°C to obtain the titanium-based part.

[0031] To achieve the above objectives, according to a second aspect of the present invention, a high-performance titanium-based component is provided.

[0032] This high-performance titanium-based component is prepared by the above-mentioned powder hot isostatic pressing method based on low-cost near-spherical bimodal powder; wherein:

[0033] The titanium-based components include pure titanium components and Ti-6Al-4V components. The Ti-6Al-4V components have a density ≥99.5%, a tensile strength of 1023.5~1058.7MPa, an elongation of 20.1%~22.5%, and a dimensional deviation ≤0.1mm.

[0034] The pure titanium parts have a density ≥99.5%, a tensile strength of 568.4~614.1MPa, an elongation of 20.6~21.8%, and a dimensional deviation ≤0.1mm.

[0035] This invention proposes a method of obtaining bimodal powder distribution using powder particle size distribution to improve the tap density of raw material powder for hot isostatic pressing, thereby increasing the compactness of the billet and ultimately achieving high-precision, low-cost fabrication of high-performance, thin-walled, complex-structure titanium-based parts. Specifically, high-performance, low-cost thin-walled, complex-structure titanium-based parts are prepared using near-spherical bimodal titanium powder or near-spherical bimodal titanium alloy powder as raw materials, combined with powder hot isostatic pressing technology.

[0036] The preparation method of this invention has the following advantages:

[0037] 1) Compared with single-peak particle size distribution powder, the bimodal particle size distribution powder proposed in this invention has a higher tap density, which can effectively improve the density of the original blank and thus improve the density of the part, and reduce the dimensional shrinkage of the blank under high temperature and high pressure during the hot isostatic pressing process, ultimately obtaining a part with better dimensional accuracy and mechanical properties.

[0038] 2) The powder particle size distribution method in this invention expands the particle size range of powders used in hot isostatic pressing (50–120 μm for single-peak powders and 30–150 μm for bi-peak powders), improving the utilization rate of powders with particle sizes <50 μm and >120 μm. Furthermore, compared to spherical powders prepared by gas atomization and plasma spheroidization methods, the near-spherical titanium-based powders used in this invention are less expensive. Therefore, the method proposed in this invention can effectively reduce the cost of raw material powders used in hot isostatic pressing technology.

[0039] 3) The powder hot isostatic pressing preparation technology used in this invention has a short process cycle, high material utilization rate, uniform and fine microstructure of the parts, and performance that can reach the level of forgings. It is an important process for preparing thin-walled complex structure titanium parts that integrate high precision and high performance.

[0040] 4) The bimodal particle size powder preparation technology proposed in this invention, which combines wet mixing of PEG10000 suspension with rotary degreasing in a furnace, can obtain bimodal particle size powder with higher flowability, uniformity and purity. It solves the problem of uneven mechanical properties of the parts caused by uneven mixing of the two powders in the traditional ball milling process, as well as the problem of introducing metal elements and impurities such as oxygen and carbon contained in the grinding balls into the powder due to long-term ball milling. In addition, the high-temperature rotary degreasing process can also dry the powder at the same time. Attached Figure Description

[0041] Various other advantages and benefits will become apparent to those skilled in the art upon reading the following detailed description of preferred embodiments. The accompanying drawings are for illustrative purposes only and are not intended to limit the invention. Furthermore, the same reference numerals denote the same parts throughout the drawings. In the drawings:

[0042] Figure 1 is a morphology diagram of the near-spherical bimodal particle size distribution titanium powder prepared in Example 1 of the present invention.

[0043] Figure 2 shows a titanium part prepared by near-net-shape powder hot isostatic pressing (NNS-HIP) technology in Example 1 of the present invention. Detailed Implementation

[0044] Exemplary embodiments of the present disclosure will now be described in more detail with reference to the accompanying drawings. While exemplary embodiments of the present disclosure are shown in the drawings, it should be understood that the present disclosure may be implemented in various forms and should not be limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the scope of the disclosure to those skilled in the art.

[0045] Powder tap density, as one of the key factors affecting the original density of the billet, significantly influences the shrinkage rate and density of hot isostatically pressed parts, thereby affecting the dimensional accuracy and mechanical properties of the parts. Therefore, developing new methods to improve the density of the original billet and thus enhance the performance and dimensional accuracy of thin-walled complex titanium alloy parts produced by powder hot isostatic pressing (POP) is crucial for advancing and widely applying titanium alloy powder hot isostatic pressing technology.

[0046] Therefore, this invention provides a method for preparing high-performance titanium-based component powder by hot isostatic pressing based on low-cost near-spherical bimodal powder.

[0047] The method for preparing high-performance titanium-based parts by hot isostatic pressing of low-cost near-spherical bimodal powder includes the following steps:

[0048] 1) Obtain near-spherical titanium-based powder with a bimodal particle size distribution; wherein the near-spherical titanium-based powder with a bimodal particle size distribution has a particle size of 30–150 μm, a flowability of 31–36 s / 50 g, and a tap density of 2.93–3.02 g / cm³. 3 .

[0049] In embodiments of the present invention, the near-spherical titanium-based powder with bimodal particle size distribution can be near-spherical titanium powder with bimodal particle size distribution or near-spherical titanium alloy powder with bimodal particle size distribution.

[0050] It is worth mentioning that the present invention uses particles with different medium particle sizes D 50 Near-spherical titanium powder or titanium alloy powder is used as raw material powder. The near-spherical powder with bimodal particle size distribution for hot isostatic pressing is prepared by wet mixing and high-temperature rotary degreasing under inert gas protection.

[0051] The preparation of the near-spherical titanium-based powder with bimodal particle size distribution in this invention includes the following steps:

[0052] 1-1) Using two different medium particle sizes D 50 Near-spherical titanium powder is used as the raw material powder, or two different medium particle sizes D 50 The raw material is a near-spherical titanium alloy powder.

[0053] In an embodiment of the present invention, the raw material powder contains two different medium particle sizes D 50Near-spherical powders (titanium powder or titanium alloy powder) are called fine powder and coarse powder, respectively. The particle size of fine powder is 30-80 μm, and the particle size of coarse powder is 80-150 μm.

[0054] As one embodiment of the present invention, the medium particle size D of the fine powder and the coarse powder 50 The ratio is 0.414:1 to 0.360:1.

[0055] In one embodiment of the present invention, the mass ratio of fine powder to coarse powder is 1:9 to 4:6.

[0056] In embodiments of the present invention, titanium alloy powder includes, but is not limited to, Ti-6Al-4V alloy powder.

[0057] 1-2) Place the raw material powder in a suspension and stir for 2-8 hours at a stirring speed of 300-600 r / min to obtain a powder mixture slurry. The stirring can be carried out under a high-purity argon protective atmosphere.

[0058] In embodiments of the present invention, the suspension is a mixture of polyethylene glycol 10000 (PEG10000) and anhydrous ethanol, or a mixture of polyethylene glycol 10000 and deionized water.

[0059] In one embodiment of the present invention, the mass of polyethylene glycol 10000 accounts for 3 to 5% of the total mass of the raw material powder.

[0060] In one embodiment of the present invention, the mass of the raw material powder accounts for 60-80% of the total mass of the powder mixture slurry.

[0061] 1-3) Under a protective atmosphere, the powder mixture slurry is degreased to obtain near-spherical titanium-based powder with a bimodal particle size distribution. The protective gas can be high-purity argon.

[0062] In an embodiment of the present invention, the degreasing temperature is 120–160°C, the heating rate is 0.5–3°C / min, and the degreasing time is 1–2 hours.

[0063] It is worth mentioning that before vacuum sealing, samples of the nearly spherical titanium-based powder with a bimodal particle size distribution were taken for relevant tests. Specifically, the morphology, particle size distribution, flowability, and tap density of the mixed powder were observed using a scanning electron microscope, a laser particle size analyzer, a Hall effect flow meter (funnel diameter 5 mm), and a tap density meter.

[0064] The bimodal particle size distribution of the near-spherical titanium-based powder has a particle size of 30–150 μm, a flowability of 31–36 s / 50 g, and a tap density of 2.93–3.02 g / cm³. 3 Its shape is nearly spherical, as shown in Figure 1.

[0065] 2) High-quality, bimodal, near-spherical titanium-based powder was packed into a well-sealed enclosure using a vibration method, and then compacted by vibration.

[0066] It is worth mentioning that before loading the near-spherical titanium-based powder with a bimodal particle size distribution, the packaging must be ultrasonically cleaned and dried sequentially. For example, the packaging can be ultrasonically cleaned in alcohol to remove surface dust and oil, and then dried after cleaning. The packaging can be made of metal.

[0067] It should be noted that after the drying process, the upper and lower end caps, the vent pipe, and the cylinder are sealed and welded, and their airtightness is tested to ensure that the airtightness of the casing is good.

[0068] Leakage rate in vacuum mode is less than 1.0 × 10⁻⁶. -9 Pa.m 3 When the air tightness is / s, the air tightness of the casing is considered to be good.

[0069] 3) After vacuuming and sealing the cladding, hot isostatic pressing is performed to obtain titanium-based parts.

[0070] In an embodiment of the present invention, a shroud thermal degassing system is used to perform vacuum treatment on the shroud, with a vacuum degree ≤1.0×10⁻⁶. -3 Pa.

[0071] It is worth mentioning that the vacuuming process includes the following steps:

[0072] Evacuate the enclosure to a vacuum level ≤1.0×10 at room temperature. -3 Pa;

[0073] Heat the sheath to 550℃, with a vacuum degree ≤1.0×10⁻⁶. -3 After Pa, keep for 5 hours to further remove moisture.

[0074] In an embodiment of the present invention, a hydraulic clamp is used in conjunction with argon arc welding to seal the vacuum tube;

[0075] In an embodiment of the present invention, the temperature of the hot isostatic pressing preparation process is 750–1000°C, the pressure is 70–120 MPa, and the holding time is 3–5 h.

[0076] After the hot isostatic pressing process is completed, the pressure is released and the temperature is cooled to below 200°C to obtain titanium-based parts.

[0077] According to a specific embodiment of the present invention, a high-performance, low-cost titanium-based component is also provided.

[0078] The high-performance, low-cost titanium-based components of this invention are prepared by the above-mentioned high-performance titanium-based component powder hot isostatic pressing method based on low-cost near-spherical bimodal powder. Specifically, the titanium-based components include pure titanium components and Ti-6Al-4V components. The Ti-6Al-4V components have a density ≥99.5%, a tensile strength of 1023.5–1058.7 MPa, an elongation of 20.1%–22.5%, and a dimensional deviation ≤0.1 mm. The pure titanium components have a density ≥99.5%, a tensile strength of 568.4–614.1 MPa, an elongation of 20.6–21.8%, and a dimensional deviation ≤0.1 mm.

[0079] The preparation method of the present invention will be described in detail below through specific embodiments.

[0080] Example 1:

[0081] Two types of near-spherical Ti-6Al-4V powders with average particle sizes ranging from 30 to 50 μm and 50 to 120 μm, respectively, were weighed at a mass ratio of 4:6. These powders were placed in a beaker containing a suspension of PEG10000 in anhydrous ethanol. The PEG10000 accounted for 3.5% of the total mass of the two powders, and the total mass of the two powders accounted for 75% of the total mass of the slurry. Under high-purity argon protection, the two powders of different particle sizes were mixed uniformly using a magnetic stirrer at a speed of 460 r / min for 4 h. The resulting mixed powder slurry was then placed in a high-temperature rotary furnace for degreasing. High-purity argon was used as the protective gas. The degreasing temperature was 150 °C, the heating rate was 2 °C / min, and the holding time was 1.5 h. After furnace cooling, near-spherical bimodal Ti-6Al-4V alloy powder with a particle size distribution was obtained and vacuum-sealed for storage. Before sealing, a small amount of powder was taken for tests on powder morphology, particle size, and flowability. The results are detailed in Table 1.

[0082] The metal sheath used in hot isostatic pressing was ultrasonically cleaned with alcohol to remove surface dust and oil, and then dried. The upper and lower end caps and the extraction pipe were then sealed to the cylinder using an argon arc welding machine. The welded sheath was visually inspected for defects such as slag inclusions, cracks, incomplete fusion, penetration, and porosity. Finally, a helium leak detector was used for further airtightness testing (leakage rate less than 1.0 × 10⁻⁶ in vacuum mode). -9 Pa.m 3 At a speed of / s, the cladding exhibits good airtightness, meeting the usage requirements. The aforementioned near-spherical bimodal Ti-6Al-4V alloy powder is loaded into the airtight cladding using a vibration method. Sufficient vibration ensures compact filling within the cladding, resulting in a high-density original billet. After powder loading, the cladding is vacuumed using a thermal degassing system. Specifically, firstly, the cladding is evacuated to a vacuum level of 1.0 × 10⁻⁶ at room temperature. -3Pa, then the shroud is placed in a pit furnace and heated to 550°C, achieving a vacuum degree of 1.0 × 10⁻⁶. -3 After vacuuming, the vacuum tube is sealed using hydraulic clamps and argon arc welding. Then, the vacuumed and sealed tube is placed in a hot isostatic pressing furnace and heated and pressurized to 750℃ and 120MPa. It is then held at this temperature and pressure for 4 hours. After the pressure is held, the pressure is released and the tube is furnace-cooled to below 200℃. The part is then removed, and its dimensional accuracy, density, tensile strength, and elongation are tested. The results are shown in Table 2.

[0083] Examples 2 and 3 used the same preparation process as Example 1, except for the particle size characteristics of the raw material powder, the use of bimodal powder, and the parameters of the hot isostatic pressing preparation process. Examples 4 and 5 used the same preparation process as Example 1, except for the composition of the raw material powder and the particle size D. 50 Bimodal powder and powder hot isostatic pressing process parameters. The properties of near-spherical bimodal powder, the properties of powder hot isostatic pressing titanium-based parts, and the preparation process parameters of bimodal powder and its parts in Examples 1-5 are summarized in Tables 1-3.

[0084] Table 1. Summary of powder properties of the bimodal particle size distribution titanium-based powders in Examples 1-5

[0085]

[0086] Table 2 summarizes the properties of titanium-based parts prepared in Examples 1-5.

[0087] Part Performance Examples 1 Example 2 Example 3 Example 4 Example 5 Part Composition Ti-6Al-4V Alloy Ti-6Al-4V Alloy Ti-6Al-4V Alloy Pure Titanium Pure Titanium Density / % 99.87 99.94 99.67 99.74 99.92 Dimensional Deviation / mm 0.07 0.05 0.09 0.08 0.06 Tensile Strength / MPa 1023.5 1058.7 1034.75 68.46 14.1 Elongation / % 20.1 22.5 21.5 20.6 21.8 surface

[0088] Table 3 Summary of raw material powder parameters and process parameters in Examples 1-5

[0089]

[0090]

[0091] The following will compare the performance of the titanium-based parts prepared in Examples 1-5 and the titanium-based parts prepared in Comparative Examples 1-6.

[0092] I. Experimental Subjects

[0093] The titanium-based parts prepared in Examples 1-5 and the titanium-based parts prepared in Comparative Examples 1-6, wherein:

[0094] Comparative Example 1:

[0095] Ti-6Al-4V alloy powder with a particle size range basically the same as that in Example 1 was used as raw material, and Ti-6Al-4V alloy parts were prepared using the same preparation process as in Example 1. The only difference was the particle size distribution characteristics of the raw material powder: the powder particle size in Example 1 showed a bimodal distribution, while the powder particle size in Comparative Example 1 showed a unimodal distribution. Detailed descriptions of the characteristics and the performance of the parts are shown in Tables 4 and 5.

[0096] Comparative Example 2:

[0097] Ti-6Al-4V alloy powder with a particle size range basically the same as that in Example 2 was used as raw material, and Ti-6Al-4V alloy parts were prepared using the same preparation process as in Example 2. The only difference was the particle size distribution characteristics of the raw material powder: the powder particle size in Example 2 showed a bimodal distribution, while the powder particle size in Comparative Example 2 showed a unimodal distribution. Detailed descriptions of the characteristics and the performance of the parts are shown in Tables 4 and 5.

[0098] Comparative Example 3:

[0099] Ti-6Al-4V alloy powder with a particle size range basically the same as that in Example 3 was used as raw material, and Ti-6Al-4V alloy parts were prepared using the same preparation process as in Example 3. The only difference was the particle size distribution characteristics of the raw material powder: the powder particle size in Example 3 showed a bimodal distribution, while the powder particle size in Comparative Example 3 showed a unimodal distribution. Detailed descriptions of the characteristics and the performance of the parts are shown in Tables 4 and 5.

[0100] Comparative Example 4:

[0101] Ti-6Al-4V alloy powder with the same particle size distribution characteristics as in Example 3 was used as the raw material, and Ti-6Al-4V alloy parts were prepared using the same preparation process as in Example 3. The only difference was the preparation method of the raw material powder: in Example 3, the raw material powder was a bimodal particle size distribution powder prepared by wet mixing with PEG10000 suspension combined with furnace rotary degreasing technology, and in Comparative Example 4, the raw material powder was a bimodal particle size distribution powder obtained by ball milling mixing. Specific characteristics and performance of the parts are detailed in Tables 4 and 5.

[0102] Comparative Example 5:

[0103] Pure titanium parts were prepared using pure titanium powder with a particle size range that was basically the same as that in Example 4, and using the same preparation process as in Example 4. The only difference was the particle size distribution characteristics of the raw material powder: the powder particle size in Example 4 showed a bimodal distribution, while the powder particle size in Comparative Example 5 showed a unimodal distribution. Detailed descriptions of the characteristics and the performance of the parts are shown in Tables 4 and 5.

[0104] Comparative Example 6:

[0105] Pure titanium parts were prepared using pure titanium powder with a particle size range that was basically the same as that in Example 5, and using the same preparation process as in Example 5. The only difference was the particle size distribution characteristics of the raw material powder: the powder particle size in Example 5 showed a bimodal distribution, while the powder particle size in Comparative Example 6 showed a unimodal distribution. Detailed descriptions of the characteristics and the performance of the parts are shown in Tables 4 and 5.

[0106] Table 4 summarizes the powder properties of the raw material powders in Comparative Examples 1–6.

[0107]

[0108]

[0109] Table 5 summarizes the properties of titanium-based parts prepared in Comparative Examples 1–6.

[0110]

[0111] Comparative analysis of the data in the table shows that the tap density of the bimodal particle size distribution titanium-based powders obtained in Examples 1-5 is 2.93-3.02 g / cm³. 3 The tap density is higher than that of the corresponding single-peak distribution powder by 2.81–2.92 g / cm³. 3 The hot isostatic pressing titanium-based parts prepared in Examples 1-5 have high density, all exceeding 99.5%; their dimensional deviations are significantly smaller than those of the parts in Comparative Examples 1-6, with values ​​in the ranges of ≤0.1 mm and 0.1-0.15 mm, respectively; they exhibit excellent mechanical properties, with the Ti-6Al-4V alloy achieving a room temperature tensile strength of 1023.5-1058.7 MPa and an elongation in the range of 20.1%-22.5%, while pure titanium has room temperature tensile strength and elongation in the ranges of 568.4-614.1 MPa and 20.6-21.8%, respectively, representing improvements of 8.23%-10.20% and 9.24%-14.21%, 11.74%-12.38%, and 10.16%-14.13%, respectively, compared to parts made from single-peak powder.

[0112] Furthermore, comparing Example 3 and Comparative Example 4, it can be found that the tap density and flowability of the bimodal powder prepared by the powder preparation method proposed in this invention are both higher than those of the bimodal powder obtained by ball milling (2.93 g / cm³). 3 >2.89g / cm 3 The density, dimensional accuracy, tensile strength and elongation of the part obtained in Example 3 were all higher than those of the part obtained in Comparative Example 4. (36s / 50g < 40s / 50g)

[0113] The above description is merely a preferred embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any variations or substitutions that can be easily conceived by those skilled in the art within the technical scope disclosed in the present invention should be included within the scope of protection of the present invention. Therefore, the scope of protection of the present invention should be determined by the scope of the claims.

Claims

1. A method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder, characterized in that, Includes the following steps: Nearly spherical titanium-based powder with a bimodal particle size distribution is obtained using a particle size distribution method; wherein, the near-spherical titanium-based powder with a bimodal particle size distribution is either near-spherical titanium powder or near-spherical titanium alloy powder with a bimodal particle size distribution; the near-spherical titanium-based powder with a bimodal particle size distribution is loaded into a casing using a vibration method; after vacuuming and sealing the casing, a titanium-based part is obtained by hot isostatic pressing; the preparation of the near-spherical titanium-based powder with a bimodal particle size distribution includes the following steps: With two different medium particle sizes D 50 Near-spherical titanium powder is used as the raw material powder, or two different medium particle sizes D 50 The near-spherical titanium alloy powder is used as the raw material powder; the raw material powder is placed in a suspension and stirred for a certain time to obtain a powder mixture slurry; the suspension is a mixture of polyethylene glycol 10000 and anhydrous ethanol, or a mixture of polyethylene glycol 10000 and deionized water; under a protective atmosphere, the powder mixture slurry is subjected to furnace rotary degreasing treatment to obtain the near-spherical titanium-based powder with bimodal particle size distribution.

2. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The near-spherical titanium-based powder with a bimodal particle size distribution has a particle size of 30-150 μm, a flowability of 31-36 s / 50 g, and a tap density of 2.93-3.02 g / cm³. 3 .

3. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1 or 2, characterized in that, The titanium alloy powder includes Ti-6Al-4V alloy powder.

4. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The raw material powder contains two different medium particle sizes D 50 The powders are referred to as fine powder and coarse powder, respectively. The fine powder has a particle size of 30~80μm, and the coarse powder has a particle size of 80~150μm.

5. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 4, characterized in that, The medium particle size D of the fine powder and the coarse powder 50 The ratio is 0.414:1 to 0.360:

1.

6. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 4, characterized in that, The mass ratio of the fine powder to the coarse powder is 1:9 to 4:

6.

7. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The mass of the polyethylene glycol 10000 accounts for 3-5% of the total mass of the raw material powder.

8. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The raw material powder accounts for 60-80% of the total mass of the powder mixture slurry.

9. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The stirring speed is 300~600 r / min, and the stirring time is 2~8 h.

10. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The stirring was carried out under a protective atmosphere of high-purity argon.

11. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The degreasing temperature is 120~160℃, the heating rate is 0.5~3℃ / min, and the degreasing time is 1~2h.

12. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The protective gas is high-purity argon.

13. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, Before loading the near-spherical titanium-based powder with a bimodal particle size distribution, the packaging is subjected to ultrasonic cleaning and drying treatment in sequence.

14. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The cladding is vacuumed using a cladding thermal degassing system, with a vacuum level ≤1.0×10⁻⁶. -3 Pa.

15. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, The hot isostatic pressing preparation process involves a temperature of 750~1000℃, a pressure of 70~120MPa, and a holding time of 3~5h.

16. The method for preparing high-performance titanium-based parts by hot isostatic pressing based on low-cost near-spherical bimodal powder as described in claim 1, characterized in that, After the hot isostatic pressing process is completed, the pressure is released and the temperature is cooled to below 200°C to obtain the titanium-based part.

17. A high-performance titanium-based component, characterized in that, It is prepared by the hot isostatic pressing method for high-performance titanium-based parts based on low-cost near-spherical bimodal powder as described in any one of claims 1-16; wherein: the titanium-based parts include pure titanium parts and Ti-6Al-4V parts, the Ti-6Al-4V parts have a density ≥99.5%, a tensile strength of 1023.5~1058.7MPa, an elongation of 20.1~22.5%, and a dimensional deviation ≤0.1mm; the pure titanium parts have a density ≥99.5%, a tensile strength of 568.4~614.1MPa, an elongation of 20.6~21.8%, and a dimensional deviation ≤0.1mm.

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