An additively manufactured quasi-continuous webbed titanium-based composite material and method thereof

Abstract

The application discloses a kind of quasi-continuous net-like titanium-based composite based on additive manufacturing and method thereof, specifically a kind of preparation method of quasi-continuous net-like titanium-based composite for adjustable reinforcing phase content and net size, belongs to the field of titanium-based composite microstructure design.The preparation operation process includes: metal and reinforcing phase powder screening and pretreatment;Low-energy ball milling powder mixing;Printing pretreatment;Setting additive manufacturing printing parameters;According to the set parameters, block printing is carried out.The method makes the net structure size, reinforcing phase content flexible and controllable, and has the characteristics of saving raw materials, simple operation, high dimensional accuracy, etc., and has better and more balanced mechanical properties after testing.

Description

Technical Field

[0001] This invention belongs to the field of microstructure design and preparation of titanium-based composite materials, specifically a titanium-based composite material with a quasi-continuous network structure based on direct energy deposition additive manufacturing and its preparation method. In this method, the size of the network structure, the content of the reinforcing phase, and the continuity of the network structure are controllable. Background Technology

[0002] Titanium-based composites are widely used in aerospace, automotive engineering, and biomedical fields due to their high specific strength, high specific modulus, and excellent high-temperature performance, corrosion resistance, and other properties. Additive manufacturing of titanium alloys, especially the duplex titanium alloy TC4, has been extensively studied and maturely applied in various fields. Due to its extremely rapid cooling rate, additively manufactured TC4 exhibits a needle-like α-phase martensitic structure, resulting in high strength but low elongation, often below 10%. For additively manufactured TC4, higher strength and a better strength-ductility balance have always been the goals of researchers. While the addition of reinforcing phases significantly improves the strength of TC4, it also causes a drastic reduction in ductility, even leading to brittle fracture. To avoid this problem, the microstructure design of titanium-based composites has become a hot research topic. Among them, titanium-based composites with network structures prepared by traditional methods, including sintering and powder metallurgy, often exhibit better strength-ductility balance, achieving a significant increase in strength while maintaining a certain degree of ductility. This patent introduces a network structure design into additive manufacturing of titanium-based composite materials and uses TiB2 as an in-situ reactive material to generate borated titanium whiskers, thus preparing a titanium-based composite material with a quasi-continuous network structure. It also has excellent properties such as high strength and high modulus, as well as high elongation. Summary of the Invention

[0003] This invention addresses the problems of high cost, complex process, and difficult and costly subsequent processing in additive manufacturing of titanium-based composite materials with a network structure. It proposes a quasi-continuous network titanium-based composite material and its method based on additive manufacturing. TiB w The reinforcing phase exhibits a quasi-continuous network structure distribution. This method allows for flexible and controllable control over the content of the reinforcing phase, the size of the network, and the continuity of the network structure, facilitating the design and preparation of materials.

[0004] In a first aspect, the present invention provides a method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing, as detailed below:

[0005] S1: Ti6Al4V metal powder and TiB2 powder, which have been vacuum dried respectively, are mixed and subjected to low-energy ball milling to achieve the embedding and adhesion of TiB2 powder on Ti6Al4V metal powder while ensuring that the powder has good sphericity and integrity; the product after ball milling is vacuum dried to obtain mixed powder.

[0006] S2: Place the mixed powder into the powder carrier tank of the additive manufacturing equipment and complete the block printing according to the set parameters.

[0007] Preferably, in step S1, the Ti6Al4V spherical metal particles have a particle size distribution of 65-150 μm, a Hall flow rate of 28.1 s / 50 g, and a loose packing density of 2.37 g / cm³. 3 The tap density is 2.75 g / cm³. 3 TiB2 particles, used as reactants for the in-situ generation of titanium boride whisker reinforcing phases, have a particle size distribution of 1-3 μm.

[0008] Preferably, the vacuum drying process is performed as follows: the material is placed in a glass dish and kept at a vacuum temperature of 120°C for one hour.

[0009] Preferably, the ball milling process in step S1 is as follows:

[0010] 59.898 g (or 59.49 g, 58.98 g, or 57.96 g) of dried and pretreated Ti6Al4V metal powder and 0.102 g (or 0.51 g, 1.02 g, or 2.04 g) of TiB2 powder were weighed out, along with 300 g of 6 mm and 10 mm grinding beads. All were ball-milled in a ceramic ball mill jar. The milling speed was 200-250 rpm (the milling speed can be gradually increased within this range as the titanium diboride content increases; higher speeds allow for better embedding of the reinforcing phase without damaging the sphericity and integrity of the TC4 particles). The ball-to-powder ratio was 5:1, the milling time was 6-8 hours, and the milling atmosphere was argon. After ball milling, the reinforcing phase TiB2 was generated in situ. w The mass fraction is 0.1% (or 0.5%, or 1%, or 2%).

[0011] The preferred embodiment of the present invention provides four sets of parameters, and one set can be selected for implementation in actual use. The four sets of parameters are: 1) 59.898 g of Ti6Al4V metal powder and 0.102 g of TiB2 powder. After ball milling, the reinforcing phase TiB2 is generated in situ. w The mass fraction is 0.1%; 2) 59.49 g of Ti6Al4V metal powder and 0.51 g of TiB2 powder, after ball milling, the reinforcing phase TiB is generated in situ. wThe mass fraction is 0.5%; 3) 58.98 g of Ti6Al4V metal powder and 1.02 g of TiB2 powder, which, after ball milling, form the reinforcing phase TiB in situ. w The mass fraction is 1%; 4) 57.96 g of Ti6Al4V metal powder and 2.04 g of TiB2 powder, after ball milling, the reinforcing phase TiB is generated in situ. w The mass fraction is 2%.

[0012] Preferably, the additive manufacturing equipment is model BLT-C400, and the pretreatment procedures before use are as follows:

[0013] Argon gas is injected into the additive manufacturing equipment for gas scrubbing to keep the oxygen content in the cabin below 200 ppm. The pressure holding is then activated to maintain a constant cabin pressure of 0.6 MPa.

[0014] As a preferred embodiment, the printing parameter setting operation of the additive manufacturing equipment before use is as follows:

[0015] Using Magic 3D modeling software, a block model for printing was created. BLT-BP software was used to set printing parameters for the block model, generating a scan path .nc file which was then stored in the additive manufacturing equipment. Specifically, the printing idle speed was set to 1000 mm / min, the printing mode to platform mode, the scanning sequence to inner infill with an outer ring, the layer thickness to 0.4 mm, the number of outer rings to 0, the spot diameter to 1 mm, the inner infill to be applied, the infill mode to continuous scanning mode, the path spacing to 1 mm, the rotation start angle to 0°, the rotation increase angle to 90°, the laser power to 750-800 W, the scanning rate to 700-800 mm / min, the powder carrier gas speed to 6 L / min, the dust removal fan speed to level 2, and the lens gas speed to 22 L / min.

[0016] In a second aspect, the present invention provides a quasi-continuous network titanium-based composite material obtained by any of the preparation methods described in the first aspect.

[0017] Compared with current methods for preparing mesh titanium-based composite materials or other structural metal-based composite materials, this invention has the following advantages:

[0018] This invention can be used for the design and preparation of metal matrix composites with quasi-continuous network structures (i.e., quasi-continuous network titanium matrix composites), representing an important research direction in the field of microstructure design of metal matrix composites. It has significant implications for additive manufacturing applications and the preparation of metal matrix composites. It possesses high academic value and great industrial application prospects. Compared with other existing methods for preparing network or semi-continuous network structure metal matrix composites, such as ion spark sintering, cumulative roll bonding, and diffusion welding, this method has the following characteristics:

[0019] 1. The preparation process is clear and has low requirements for the external environment. In the ball milling and additive manufacturing processes, both the metal powder and the bulk material are in a closed environment and are protected by argon gas, making them insensitive to external environmental factors.

[0020] 2. Mature and easy-to-control processes. The ball milling process in the preparation flow is mature, its principle is easy to understand, has few variables, and is easy to control. The additive manufacturing process and equipment technology are mature and stable, and the preparation flow is implemented through software, making operation simple.

[0021] 3. The manufacturing process is simple, saving time and raw materials. Additive manufacturing can achieve near-net-shape forming of parts, avoiding subsequent processing and post-processing, thus saving on raw material and time costs.

[0022] 4. High design flexibility and numerous design variables. This method allows for relatively flexible design and adjustment of design variables such as the content of the reinforcing phase, the size of the network structure, and the continuity of the network structure regions, without increasing the preparation process or time.

[0023] 5. Wide applicability. This method is applicable to various alloy systems. It can be used to prepare semi-continuous structures using different types of metal powders, and other types of reinforcing phase particles can be added to prepare different kinds of metal matrix composites.

[0024] This invention is used to prepare TC4-TiB w Quasi-continuous network structure titanium-based composite material. Attached Figure Description

[0025] Figure 1 TC4 powder ( Figure 1 (a)), a mixture of TC4 and TiB2 ball-milled powder ( Figure 1 (b) Scanning electron microscope image.

[0026] Figure 2 This is a photograph of the composite material block prepared in Example 1.

[0027] Figure 3 The image shown is a scanning electron microscope image of the quasi-continuous network structure titanium-based composite material prepared in Example 1, wherein the content of the reinforcing phase is 0.1%. Due to the low content of the reinforcing phase, the network structure is not obvious, and the reinforcing phase is evenly distributed.

[0028] Figure 4The figures show the tensile stress-strain curves of four quasi-continuous network structure titanium matrix composites from Examples 1 to 4. The black line represents the tensile stress-strain curve of ordinary TC4 alloy prepared by direct laser stereolithography additive manufacturing; the red line represents the tensile stress-strain curve of the quasi-continuous network structure titanium matrix composite prepared by direct laser stereolithography in Example 1; the blue line represents the tensile stress-strain curve of the quasi-continuous network structure titanium matrix composite prepared by direct laser stereolithography in Example 2; the green line represents the tensile stress-strain curve of the quasi-continuous network structure titanium matrix composite prepared by direct laser stereolithography in Example 3; and the purple line represents the tensile stress-strain curve of the quasi-continuous network structure titanium matrix composite prepared by direct laser stereolithography in Example 4.

[0029] Figure 5 The image shows a scanning electron microscope image of the quasi-continuous network structure titanium-based composite material prepared in Example 2, in which the reinforcing phase content is 0.5%, the network structure is obvious, the network size is large, and the continuity is low.

[0030] Figure 6 The image shows a scanning electron microscope image of the quasi-continuous network structure titanium-based composite material prepared in Example 3, in which the reinforcing phase content is 1%, the network structure is obvious, the network size is small, and the continuity is high.

[0031] Figure 7 The image shows a scanning electron microscope image of the quasi-continuous network structure titanium-based composite material prepared in Example 4, in which the reinforcing phase content is 2%, the network structure is obvious, the network size is small, and the continuity is high. Detailed Implementation

[0032] The present invention will be further described and illustrated below with reference to the accompanying drawings and specific embodiments. The technical features of each embodiment of the present invention can be combined accordingly, provided that there is no mutual conflict.

[0033] This invention provides a method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing. The method mainly includes: S1, mixing Ti6Al4V metal powder and TiB2 powder, which have undergone vacuum drying, and then performing low-energy ball milling to achieve embedding and adhesion of TiB2 powder onto the Ti6Al4V metal powder; and vacuum drying the ball-milled product to obtain a mixed powder; S2, using additive manufacturing equipment, placing the mixed powder into a powder carrier container and performing block printing according to set parameters to obtain the quasi-continuous network titanium-based composite material. The preparation method is specifically carried out according to the following steps:

[0034] I. Screening and Pretreatment of Metal and Reinforcing Phase Powders. Laser additive manufacturing methods place high demands on the flowability and sphericity of metal powders. In this invention, spherical Ti6Al4V (TC4) metal particles with a particle size distribution of 65-150 μm (D10=58.84μm, D50=84.61μm, D90=117.5μm), a Hall flow rate of 28.1 s / 50g, and a loose packing density of 2.37 g / cm³ are preferably selected. 3 The tap density is 2.75 g / cm³. 3 TiB2 particles with a particle size distribution of 1-3 μm were selected as in-situ generated titanium boride whiskers (TiB2). w The reactants for the reinforcing phase were prepared by placing TC4 metal powder and TiB2 powder separately into glass dishes and then placing them in a vacuum chamber for incubation. The powders were then dried and pretreated by maintaining the temperature at 120°C for one hour under vacuum.

[0035] Here, TC4 powder with a particle size of 65-150 μm and D50 = 84.61 μm is preferably selected. TiB2 powder with a particle size of 1-3 μm is also preferred. During the additive manufacturing process, titanium boride whiskers are generated in situ, and the whisker distribution exhibits a network structure.

[0036] II. Low-energy ball milling and powder mixing. Weigh a certain proportion of TC4 metal powder ( Figure 1 (a) The TiB2 powder is mixed with TiB2 powder and then ball-milled at low energy to achieve a relatively uniform embedding and adhesion of TiB2 particles onto TC4 particles while ensuring good sphericity and integrity of the powder. In this invention, preferably 59.898 g (or 59.49 g, or 58.98 g, or 57.96 g) of TC4 powder and 0.102 g (or 0.51 g, or 1.02 g, or 2.04 g) of TiB2 are weighed, and 300 g of ball milling beads with particle sizes of 6 mm and 10 mm are selected and ball-milled in a ceramic ball milling jar. The ball milling speed is 200-250 rpm (the ball milling speed can be gradually increased within the range as the titanium diboride content increases; higher speeds can better achieve the embedding of the reinforcing phase without damaging the sphericity and integrity of the TC4 particles), the ball-to-material ratio is 5:1, the ball milling time is 6-8 hours, and the ball milling atmosphere is argon. This method can achieve a good and uniform embedding and adhesion effect while ensuring good sphericity and integrity. Figure 1 (b)).

[0037] Here, 59.898 g (or 59.49 g, or 58.98 g, or 57.96 g) of TC4 powder and 0.102 g (or 0.51 g, or 1.02 g, or 2.04 g) of TiB2 are preferably ball-milled to induce in-situ formation of the reinforcing phase TiB2. wThe mass fraction is 0.1% (or 0.5%, 1%, or 2%). The preferred ball milling parameters are 200-250 revolutions per minute, a ball-to-powder ratio of 5:1, a milling time of 6-8 hours, an argon atmosphere, and a mixture of 6mm and 10mm ball sizes. This is because, after conducting 18 orthogonal ball milling experiments, including parameters related to milling speed, time, and ball-to-powder ratio, and observing the powder particles after milling using scanning electron microscopy, the above parameters were found to be the optimal ball milling parameters. These parameters can achieve a good and uniform interlocking effect between TC4 and TiB2 powders while ensuring sphericity and integrity.

[0038] III. Printing Pretreatment. The mixed powder obtained in step II is placed in a glass dish and then placed in a vacuum chamber for vacuum insulation. Under vacuum conditions, it is kept at 120°C for one hour to ensure the powder is dry. The BLT-C400 additive manufacturing equipment used is then purged with argon gas to maintain the oxygen content in the chamber below 200 ppm. Pressure maintenance is then initiated to maintain a constant chamber pressure of 0.6 MPa.

[0039] IV. Setting Additive Manufacturing Printing Parameters. Using Magic 3D modeling software, a block model for printing is created. Using BLT-BP software, printing parameters are set for the block model, generating a scan path .nc file and saving it to the BLT-C400. Specifically, the printing idle speed is set to 1000 mm / min, the printing mode to platform mode, the scanning sequence to inner infill with an outer ring, the layer thickness to 0.4 mm, the number of outer rings to 0, the spot diameter to 1 mm, inner infill selected, the infill mode to continuous scanning mode, the path spacing to 1 mm, the rotation start angle to 0°, the rotation increment angle to 90°, the laser power to 750-800 W, the scanning rate to 700-800 mm / min, the powder carrier gas speed to 6 L / min, the dust collector fan speed to level 2, and the lens gas speed to 22 L / min.

[0040] Through single-pass and double-pass additive manufacturing experiments with parameters including laser power and scanning rate, the optimal path spacing and layer thickness were obtained for each set of parameters. Ten orthogonal experiments were conducted on printing parameters including laser power, scanning speed, and powder feeding speed, and the above parameters were determined to be the optimal printing parameters, achieving a bulk density of 99.97% and a maximum pore size of 70 micrometers.

[0041] V. Using the above parameters, print to obtain a quasi-continuous network structure titanium-based composite material.

[0042] Example 1

[0043] This embodiment prepares a quasi-continuous network titanium-based composite material. The specific preparation method is carried out according to the following steps:

[0044] I. Select Ti6Al4V (TC4) spherical metal particles with a particle size distribution of 65-150 μm (D10=58.84μm, D50=84.61μm, D90=117.5μm), a Hall flow rate of 28.1 s / 50g, and a loose packing density of 2.37 g / cm³. 3 The tap density is 2.75 g / cm³. 3 TiB2 particles with a particle size distribution of 1-3 μm were selected as in-situ generated titanium boride whiskers (TiB2). w The reactants for the reinforcing phase were prepared by placing TC4 metal powder and TiB2 powder separately into glass dishes and then placing them in a vacuum chamber for incubation. The powders were then dried and pretreated by maintaining the temperature at 120°C for one hour under vacuum.

[0045] 2. Weigh 59.898g of TC4 powder and 0.102g of TiB2, and select 300g of grinding balls with particle sizes of 6mm and 10mm. Grind the mixture in a ceramic ball mill jar. Set the grinding speed to 200 rpm, the ball-to-powder ratio to 5:1, the grinding time to 8 hours, and the grinding atmosphere to argon.

[0046] 3. Place the mixed powder obtained in step 2 into a glass dish and then place it in a vacuum chamber for vacuum insulation. Maintain the temperature at 120°C for one hour under vacuum to ensure the powder is dry. Purge the BLT-C400 additive manufacturing equipment by filling it with argon gas to keep the oxygen content in the chamber below 200 ppm. Then, activate the pressure holding function to maintain a constant chamber pressure of 0.6 MPa.

[0047] IV. Using Magic 3D modeling software, a 55mm × 26mm × 5mm cuboid model was created. The BLT-BP software was used to set the printing parameters for the model, generating a scan path .nc file and saving it to the BLT-C400. The settings included: print idle speed of 1000mm / min, print mode of platform mode, scan sequence of inner fill plus outer ring, layer thickness of 0.4mm, number of outer rings of 0, spot diameter of 1mm, selection of inner fill, continuous scan mode, path spacing of 1mm, rotation start angle of 0°, rotation increase angle of 90°, laser power of 750W, scan rate of 700mm / min, toner gas speed of 6L / min, dust fan speed of level 2, and lens gas speed of 22L / min.

[0048] 5. Place the mixed powder obtained in step 3 into the toner carrier tank, set the toner feeder rotation speed to 2%, and start printing. After completing the printing operation, you will obtain TC4 / TiB. w Dual-structure composite materials ( Figure 2 ).

[0049] This embodiment prepared a titanium matrix composite material with a quasi-continuous network structure (i.e., a quasi-continuous network titanium matrix composite material) by ball milling and additive manufacturing. However, due to the low content of the reinforcing phase, the network structure was not obvious. Figure 3 In this embodiment, a tensile stress-strain curve is obtained through a tensile test. Figure 4 Red, TC4-0.1% TiB w As can be seen, the modulus and strength of the quasi-continuous network structure titanium-based composite material prepared in this embodiment are improved to a certain extent, with the strength reaching 1132 MPa and the elongation reaching 9%. This means that the current quasi-continuous network structure design is conducive to improving the strength and modulus of the material, and the toughness is not greatly reduced.

[0050] Example 2

[0051] In this embodiment, a quasi-continuous network titanium-based composite material was prepared. The specific preparation method was basically the same as that in Example 1, except that in step two, 59.49g of TC4 powder and 0.51g of TiB2 powder were selected for ball milling, and it was expected that the content of TiB reinforcing phase in the prepared composite material would be 0.5%.

[0052] This embodiment prepared TiB w A quasi-continuous network structure titanium matrix composite material in which the reinforcing phase exhibits a network distribution. Scanning electron microscopy images of this composite material are shown below. Figure 5 As shown, the reinforcing phase exhibits a network structure distribution in the network region, without aggregation. The tensile curve results in this embodiment are as follows: Figure 4 Blue line (TC4-0.5% TiB) w As shown in the figure, the comparison shows that the material has a strength of 1222 MPa and an elongation of 11%. This structural design significantly improves the material's strength and modulus, while slightly improving its toughness, achieving the effect of simultaneous strengthening and toughening.

[0053] Example 3

[0054] In this embodiment, a quasi-continuous network titanium-based composite material was prepared. The specific preparation method was basically the same as that in Example 1, except that in step two, 58.98g of TC4 powder and 1.02g of TiB2 powder were selected for ball milling, and it was expected that the content of TiB reinforcing phase in the prepared composite material would be 1%.

[0055] This embodiment prepared TiB w A quasi-continuous network structure titanium matrix composite material in which the reinforcing phase exhibits a network distribution. Scanning electron microscopy images of this composite material are shown below. Figure 6 As shown, the reinforcing phase exhibits a network structure distribution in the network region, with no obvious aggregation. The tensile curve results in this embodiment are as follows: Figure 4 Green line (TC4-1% TiB)w As shown in the figure, the comparison shows that the material has a strength of 1180MPa and an elongation of 9%. This structural design significantly improves the material's strength and modulus, but slightly reduces its toughness.

[0056] Example 4

[0057] In this embodiment, a quasi-continuous network titanium-based composite material was prepared. The specific preparation method was basically the same as that in Example 1, except that in step two, 57.96g of TC4 powder and 2.04g of TiB2 powder were selected for ball milling, and it was expected that the content of TiB reinforcing phase in the prepared composite material would be 2%.

[0058] This embodiment prepared TiB w A quasi-continuous network structure titanium matrix composite material in which the reinforcing phase exhibits a network distribution. Scanning electron microscopy images of this composite material are shown below. Figure 7 As shown, the reinforcing phase exhibits a network structure distribution in the network region, with no obvious aggregation. The tensile curve results in this embodiment are as follows: Figure 4 Purple line (TC4-2% TiB) w As shown in the figure, the comparison shows that the material has a strength of 1231 MPa and an elongation of 6%. This structural design significantly improves the material's strength and modulus, but reduces its toughness to some extent.

[0059] The embodiments described above are merely preferred embodiments of the present invention and are not intended to limit the invention. Those skilled in the art can make various changes and modifications without departing from the spirit and scope of the invention. Therefore, all technical solutions obtained through equivalent substitution or transformation fall within the protection scope of the present invention.

Claims

1. A method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing, characterized in that, Specifically as follows: S1: Ti6Al4V metal powder and TiB2 powder, which have been vacuum dried respectively, are mixed and subjected to low-energy ball milling to achieve the embedding and adhesion of TiB2 powder on Ti6Al4V metal powder while ensuring that the powder has good sphericity and integrity; the product after ball milling is vacuum dried to obtain mixed powder. S2: Using additive manufacturing equipment, the mixed powder is placed into a powder carrier tank, and block printing is completed according to the set parameters to obtain a quasi-continuous network titanium-based composite material. In step S1, the Ti6Al4V spherical metal particles have a particle size distribution of 75-160 μm, a Hall flow rate of 28.1 s / 50 g, and a loose packing density of 2.37 g / cm³. 3 The tap density is 2.75 g / cm³. 3 The particle size distribution of TiB2 particles is 1-3 μm. The ball milling process in step S1 is as follows: Ti6Al4V metal powder and TiB2 powder, which have undergone drying and pretreatment, were weighed separately. 300 g of ball milling beads with particle sizes of 6 mm and 10 mm were selected and ball milled together in a ceramic ball milling jar. The ball milling speed was 200-250 rpm, the ball-to-material ratio was 5:1, the ball milling time was 6-8 h, and the ball milling atmosphere was argon. During the ball milling process, 59.898 g of Ti6Al4V metal powder and 0.102 g of TiB2 powder were weighed out. At this time, the reinforcing phase TiB2 was generated in situ after ball milling. w The mass fraction is 0.1%; or during ball milling, 59.49 g of Ti6Al4V metal powder and 0.51 g of TiB2 powder are weighed, and the reinforcing phase TiB2 is generated in situ after ball milling. w The mass fraction is 0.5%; or during ball milling, 58.98 g of Ti6Al4V metal powder and 1.02 g of TiB2 powder are weighed, and the reinforcing phase TiB2 is generated in situ after ball milling. w The mass fraction is 1%; or during ball milling, 57.96 g of Ti6Al4V metal powder and 2.04 g of TiB2 powder are weighed, and the reinforcing phase TiB2 is generated in situ after ball milling. w The mass fraction is 2%; by changing the content of the reinforcing phase, the size of the network structure and the continuity of the network structure region in the obtained additive manufacturing-based quasi-continuous network titanium matrix composite can be adjusted.

2. The method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing according to claim 1, characterized in that, The vacuum drying process is as follows: the material is placed in a glass dish and kept at 120°C in a vacuum environment for one hour.

3. The method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing according to claim 1, characterized in that, The additive manufacturing equipment is model BLT-C400. The pretreatment procedures before use are as follows: Argon gas is injected into the additive manufacturing equipment for gas scrubbing to keep the oxygen content in the cabin below 200 ppm. The pressure holding is then activated to maintain a constant cabin pressure of 0.6 MPa.

4. The method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing according to claim 1, characterized in that, The specific steps for setting the printing parameters of the additive manufacturing equipment before use are as follows: Using Magic 3D modeling software, a block model for printing was created. BLT-BP software was used to set the printing parameters for the model, generating a scan path .nc file which was then stored in the additive manufacturing equipment. Specifically, the printing idle speed was set to 1000 mm / min, the printing mode to platform mode, the scanning sequence to inner infill with an outer ring, the layer thickness to 0.4 mm, the number of outer rings to 0, the spot diameter to 1 mm, the inner infill to be applied, the infill mode to continuous scanning mode, the path spacing to 1 mm, the rotation start angle to 0°, the rotation increase angle to 90°, the laser power to 750-800 W, the scanning rate to 700-800 mm / min, the powder carrier gas speed to 6 L / min, the dust removal fan speed to level 2, and the lens gas speed to 22 L / min.

5. The method for preparing a quasi-continuous network titanium-based composite material based on additive manufacturing according to claim 1, characterized in that, In step S2, the block printing operation of the mixed powder is specifically as follows: Using Magic modeling software, a block model was created. BLT-BP software was used to set printing parameters for the block model, generating a scan path .nc file which was then stored in the additive manufacturing equipment. The settings included: a print idle speed of 1000 mm / min, a platform mode, an inner fill with an outer ring, a layer thickness of 0.4 mm, 0 outer rings, a spot diameter of 1 mm, application of inner fill, continuous scanning mode, a path spacing of 1 mm, a rotation start angle of 0°, a rotation increment angle of 90°, a laser power of 750-800 W, a scanning rate of 700-800 mm / min, a powder-carrying gas velocity of 6 L / min, a dust removal fan speed of level 2, and a lens gas velocity of 22 L / min. Printing then commenced.

6. A quasi-continuous network titanium-based composite material obtained by any one of the preparation methods described in claims 1 to 5.

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