CN116727684A - A TiAl-based lightweight high-temperature material based on laser 3D printing and its preparation method - Google Patents

Abstract

The invention discloses a TiAl-based lightweight high-temperature material based on laser 3D printing and a preparation method thereof. The TiAl-based composite powder components include nano ceramic particle reinforcement phase, Ti6Al4V alloy powder dilution phase, and TiAl alloy powder matrix phase, wherein nano The ceramic particle reinforcement phase is either Si ₃ N ₄ or LaB _6. The selected nano ceramic reinforcement phase can be used as a grain heterogeneous nucleation agent and oxygen scavenger in the high-temperature dynamic melt pool formed by laser. On the one hand, By promoting the nucleation of a large number of matrix grains, it helps to achieve the transformation from columnar crystals to equiaxed crystals, refines the grains, and improves the strength of the matrix. On the other hand, it consumes dissolved oxygen components in the molten pool through in-situ reactions, which helps Improve the wettability and bonding strength of the melt channel interface, and the nano-oxide particles formed at the same time can further strengthen the matrix and avoid performance deterioration caused by adding too much; Ti6Al4V alloy powder is added to the matrix powder as a dilute phase to enhance the β phase with better plasticity in the solidification structure. stability and reduce the brittleness of the matrix structure.

Description

A TiAl-based lightweight high-temperature material based on laser 3D printing and its preparation method

Technical field

The invention belongs to the technical field of laser 3D printing, and specifically relates to a TiAl-based lightweight high-temperature material based on laser 3D printing and a preparation method thereof.

Background technique

TiAl-based alloy has low density, high melting point, high specific strength and specific stiffness, excellent creep resistance, anti-oxidation and anti-fatigue properties. It is a type of lightweight high-temperature alloy structural material with excellent performance, and its comprehensive performance is better than that of traditional nickel. Based on high-temperature alloys, it has been gradually used in high-temperature-resistant parts in aerospace and vehicle engineering, as well as wings and shells of ultra-high-speed aircraft. However, the low room temperature plasticity and toughness of TiAl alloy significantly reduces its processing and formability, severely limiting the practical application of TiAl alloy. Since its emergence in the 1980s, additive manufacturing (or 3D printing) technology has developed over decades and has become an important part of the current international advanced manufacturing technology frontier and intelligent manufacturing technology system. As one of the mainstream metal additive manufacturing technologies, powder bed laser selective melting technology based on layer-by-layer powder spreading, line-by-line scanning, and layer-by-layer melting/solidification provides an efficient and sustainable technical approach for the precision forming of three-dimensional complex components. , which can effectively solve the precision forming problems of complex components of difficult-to-machine materials such as TiAl alloys.

In the research on laser additive manufacturing of TiAl-based alloys, the current main difficulty lies in the obvious crack tendency during the forming process. Ti and Al components will form a variety of intermetallic compounds during the laser melting process, such as TiAl, Ti ₃ Al, Ti ₅ Al ₃ , etc. These phases have both metallic bond and covalent bond properties, and are highly hard and brittle as well as needle-like. The growth morphology is very easy to induce the formation and expansion of cracks. Especially in the laser forming process with extremely high temperature gradient and cooling rate, the crack sensitivity is more significant. Easing the temperature gradient and cooling rate is an effective way to suppress the occurrence of cracks in the laser forming process. The main methods include optimizing process parameters and increasing the substrate preheating temperature. However, the improvement effect of the former is relatively limited, while the latter often needs to be raised to 800°C. and above, a special preheating device needs to be customized, which causes a sudden increase in manufacturing costs and also causes serious burning loss of the Al element.

Contents of the invention

The purpose of this section is to outline some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. Some simplifications or omissions may be made in this section, the abstract and the title of the invention to avoid obscuring the purpose of this section, the abstract and the title of the invention, and such simplifications or omissions cannot be used to limit the scope of the invention.

In view of the above and/or problems existing in the prior art, the present invention is proposed.

Therefore, the purpose of the present invention is to overcome the shortcomings of the existing technology and provide a TiAl-based lightweight high-temperature material based on laser 3D printing.

In order to solve the above technical problems, the present invention provides the following technical solution: TiAl-based lightweight high-temperature materials are obtained from TiAl-based composite powder through powder bed laser 3D printing; the TiAl-based composite powder includes nano-ceramic particle reinforced phases. , Ti6Al4V alloy powder dilute phase and TiAl alloy powder matrix phase, in which the addition amount of nanoceramic particle reinforcement phase is within the range of 2wt.%, and the content of the Ti6Al4V alloy powder diluted phase is within the range of 25wt.%; the laser forming process parameters are: laser power is within Between 150-250W, the scanning speed is between 200-375mm/s, the scanning spacing is 100μm and the powder layer thickness is 50μm; the body energy density is controlled at 133-150J/mm ³ ; among them, the body energy density η=P/ (vdh), where P is the laser power, v is the scanning speed, d is the powder layer thickness, and h is the scanning distance.

As a preferred solution of the TiAl-based lightweight high-temperature material of the present invention, the nano-ceramic particle reinforced phase content is 0.3-2wt.%, the Ti6Al4V alloy powder diluted phase content is 15-25wt.%, and the rest is TiAl Alloy powder matrix phase.

As a preferred solution of the TiAl-based lightweight high-temperature material of the present invention, the nanoceramic particle reinforcement phase is Si ₃ N ₄ or LaB ₆ , the average particle size range is 50 nm, and the purity is above 99.9%.

As a preferred solution of the TiAl-based lightweight high-temperature material of the present invention, the average particle size range of the dilute phase of the Ti6Al4V alloy powder is 25 μm, the sphericity is >95%, and other elemental impurities are controlled below 0.1wt.%.

As a preferred solution of the TiAl-based lightweight high-temperature material of the present invention, the TiAl alloy powder matrix phase is a nearly equiatomic ratio titanium-aluminum alloy, in which the mole fraction of Al is between 45-48 at.%, and other elemental impurities Control it below 0.1wt.%, the rest is Ti component, the average particle size range is 20-30μm, and the sphericity is >95%.

Another object of the present invention is to solve the deficiencies in the existing technology and provide a method for preparing TiAl-based lightweight high-temperature materials based on laser 3D printing.

In order to solve the above technical problems, the present invention provides the following technical solution: a method for preparing TiAl-based lightweight high-temperature materials based on laser 3D printing as claimed in claim 1, characterized in that: the preparation method includes:

The nanoceramic particles, Ti6Al4V alloy powder and TiAl alloy powder are mixed in proportions and placed in a ball mill. The ball mill is evacuated and argon gas is introduced, and the air pressure is controlled at 0.4-0.6MPa; then the mixed powder is subjected to intermittent After ball milling, TiAl-based composite powder is obtained, which is then laser formed and solidified.

As a preferred version of the preparation method of the present invention, the ball mill uses a planetary ball mill, the ball milling medium is corundum ceramic balls, the ball milling tank uses corundum ceramic tanks, and the ball-to-material ratio during the ball milling process is 1 to 2.5 :1. The ball milling speed is 200~300r/min, and the ball milling time is 2-4h; the ball milling input energy and total number of rotations are controlled at 1544~3016J/g and 24~48×10 ³ r respectively.

As a preferred version of the preparation method of the present invention, wherein: the ball mill input energy E _t

where f is the collision frequency, w _d and w _t are the angular velocities of the main disk and tank of the ball mill respectively, E _b is the kinetic energy of the grinding ball, M _p is the powder mass, m _b and v _b are the mass and absolute speed of the grinding ball, R _d and R _t are the gyration radii of the main disk and the tank of the ball mill respectively, r _b and d _b are the radius and diameter of the grinding balls, D _t and H _t are the diameter and height of the tank respectively, N _b is the number of grinding balls numbers, k and ε are constants (equal to 1 and 1.134 respectively);

Among them, the total number of rotations λ is the number of rotations of the main disk of the ball mill, λ = nt, where n is the ball milling speed and t is the ball milling time.

As a preferred solution of the preparation method of the present invention, the laser forming and solidification of the TiAl-based composite powder mainly includes three-dimensional solid modeling, path planning, slicing and layer-by-layer powder spreading and laser scanning and solidification processes;

Wherein, the thickness of the powder layer involved in the layer-by-layer powder spreading is set to 50 μm;

Among them, the laser scanning curing involves main laser process parameter settings including laser power between 150 and 250W, scanning speed between 200 and -600mm/s, and scanning spacing of 100μm; volume energy density is controlled at 133~150J. /mm ³ .

As a preferred solution of the preparation method of the present invention, the laser scanning curing also involves a laser scanning strategy. Here, an island scanning + interlayer scanning vector rotation composite strategy is selected; where the side length of the island area is 5 to 10 mm. , the inter-layer rotation angle is 45~90°;

Among them, laser scanning curing also involves substrate preheating, and the substrate temperature is set at 200°C.

Beneficial effects of the present invention:

(1) The TiAl-based composite material provided by the present invention is obtained from TiAl-based composite powder through powder bed laser 3D printing. The optimized powder composition design and laser forming process ensure that the final formed part is nearly fully dense and has no obvious Cracks occur. The components of the TiAl-based composite powder include nano-ceramic particle reinforcement phase, Ti6Al4V alloy powder dilution phase, and TiAl alloy powder matrix phase. The nano-ceramic particle reinforcement phase is either Si ₃ N ₄ or LaB _6. The selected nano-ceramic The enhanced phase can be used as a grain heterogeneous nucleation agent and oxygen scavenger in the high-temperature dynamic melt pool formed by laser. On the one hand, it helps to achieve the transformation from columnar crystals to equiaxed crystals by promoting the nucleation of a large number of matrix grains, and also Refine the grains and improve the strength of the matrix. On the other hand, the dissolved oxygen component in the molten pool is consumed through in-situ reaction, which helps to improve the wettability and bonding strength of the molten channel interface. The nano-oxide particles formed at the same time can further strengthen the matrix. Its content is controlled at 0.3-2wt.% to avoid performance deterioration caused by adding too much; Ti6Al4V alloy powder is added to the matrix powder as a dilute phase to reduce the Al component content in the matrix and improve the stability of the β phase with better plasticity in the solidification structure. properties, reducing the brittleness of the matrix structure, and its content is controlled at 15-25wt.% to ensure the dominant position of the TiAl matrix phase.

(2) The TiAl-based composite powder provided by the present invention is prepared by a mechanical ball milling method. Different from the traditional single-factor control method, the present invention proposes a comprehensive parameter control strategy based on the joint control of the ball mill input energy and the total number of rotations of the main disk. , effectively realizing the preparation of high-quality composite powder that meets the powder bed type laser 3D printing process. The obtained composite powder has high sphericity, uniform composition, low oxygen content, and high powder bed quality.

(3) The laser 3D printed high-performance crack-free TiAl-based composite material provided by the present invention further achieves good forming quality and high density by optimizing the energy density of the laser formed body and the laser scanning forming strategy. Its role is reflected in the effective control of multiple physical fields such as the dynamic molten pool temperature field, solute field and stress field, avoiding the accumulation of large amounts of local heat and the formation of ultra-high temperature gradients, and can play a very good role in inhibiting the formation of thermal cracks.

Description of drawings

In order to explain the technical solutions of the embodiments of the present invention more clearly, the drawings needed to be used in the description of the embodiments will be briefly introduced below. Obviously, the drawings in the following description are only some embodiments of the present invention. Those of ordinary skill in the art can also obtain other drawings based on these drawings without exerting any creative effort. in:

Figure 1 SEM photo of the TiAl-based composite powder prepared in Example 1 of the present invention;

Figure 2 is a metallographic photograph of the cross section of a laser 3D printed TiAl-based composite material sample in Example 1 of the present invention;

Figure 3 is an SEM photo of the TiAl-based composite powder prepared in Example 2 of the present invention;

Figure 4 is a metallographic photograph of the cross section of a laser 3D printed TiAl-based composite material sample in Example 2 of the present invention;

Figure 5 is an SEM photo of the TiAl-based composite powder prepared in Example 3 of the present invention;

Figure 6 is a metallographic photograph of the cross section of a laser 3D printed TiAl-based composite material sample in Example 3 of the present invention;

Figure 7 SEM photo of the TiAl-based alloy powder prepared in the comparative example of the present invention;

Figure 8 is a metallographic photo of the cross section of the laser 3D printed TiAl-based alloy sample in the comparative example of the present invention.

Detailed ways

In order to make the above-mentioned objects, features and advantages of the present invention more obvious and understandable, the specific implementation modes of the present invention will be described in detail below in conjunction with the examples in the description.

Many specific details are set forth in the following description to fully understand the present invention. However, the present invention can also be implemented in other ways different from those described here. Those skilled in the art can do so without departing from the connotation of the present invention. Similar generalizations are made, and therefore the present invention is not limited to the specific embodiments disclosed below.

Second, reference herein to "one embodiment" or "an embodiment" refers to a specific feature, structure, or characteristic that may be included in at least one implementation of the present invention. "In one embodiment" appearing in different places in this specification does not all refer to the same embodiment, nor is it a separate or selective embodiment that is mutually exclusive with other embodiments.

Example 1

The purpose of the present invention is to provide a crack-free TiAl-based lightweight high-temperature material based on laser 3D printing. The TiAl-based lightweight high-temperature material is obtained from TiAl-based composite powder through powder bed type laser 3D printing.

Nano-Si ₃ N ₄ particles (content: 0.3wt.%), Ti6Al4V alloy powder (content: 15wt.%) and TiAl alloy powder (Al molar content: 45at.%) are mixed in proportions and placed in a ball mill. The ball mill is evacuated and argon gas is introduced, and the air pressure is controlled at 0.4MPa; then the mixed powder is subjected to intermittent ball milling, the ball-to-material ratio is 2.5:1, the ball milling speed is 250r/min, and the ball milling time is 2h. At this time, the ball mill input The energy and total number of rotations are 3016J/g and 30×10 ³ r respectively; the finally obtained TiAl-based composite powder is shown in Figure 1. The particles still maintain a high sphericity, and the nanoceramic particles are evenly distributed in the matrix powder. surface;

In the subsequent laser 3D printing process, the laser forming process parameters are optimized as follows: laser power is 150W, scanning speed is 200mm/s, scanning spacing is 100μm, and powder layer thickness is 50μm. At this time, the volume energy density is 150J/mm ³ ; The substrate is preheated at 200°C, and the laser scanning strategy is a composite strategy of island scanning + interlayer scanning vector rotation; the side length of the island area is 10mm, and the interlayer rotation angle is 45°. The cross-section metallographic photo of the formed sample is shown in Figure 2. It can be seen that there is no obvious crack formation inside the sample, and the density of the sample is relatively high.

Example 2

The purpose of the present invention is to provide a crack-free TiAl-based lightweight high-temperature material based on laser 3D printing. The TiAl-based lightweight high-temperature material is obtained from TiAl-based composite powder through powder bed type laser 3D printing.

Nano-Si ₃ N ₄ particles (content: 0.8wt.%), Ti6Al4V alloy powder (content: 20wt.%) and TiAl alloy powder (Al molar content: 47at.%) are mixed in proportions and placed in a ball mill. The ball mill is evacuated and argon gas is introduced, and the air pressure is controlled at 0.5MPa; then the mixed powder is subjected to intermittent ball milling, the ball-to-material ratio is 1:1, the ball milling speed is 300r/min, and the ball milling time is 2h. At this time, the ball milling input The energy and total number of rotations are 2084J/g and 36×10 ³ r respectively; the finally obtained TiAl-based composite powder is shown in Figure 3. The particles still maintain a high sphericity, and the nanoceramic particles are evenly distributed in the matrix powder. surface;

In the subsequent laser 3D printing process, the laser forming process parameters were optimized as follows: the laser power was 250W, the scanning speed was 375mm/s, the scanning spacing was 100μm, and the powder layer thickness was 50μm. At this time, the volume energy density was 133J/mm. ³ ; The substrate is preheated at 200°C, and the laser scanning strategy is a composite strategy of island scanning + interlayer scanning vector rotation; the side length of the island area is 6mm, and the interlayer rotation angle is 67°. The cross-sectional metallographic photo of the formed sample is shown in Figure 4. It can be seen that there are basically no cracks formed inside the sample, and the density of the sample is relatively high.

Example 3

The purpose of the present invention is to provide a crack-free TiAl-based lightweight high-temperature material based on laser 3D printing. The TiAl-based lightweight high-temperature material is obtained from TiAl-based composite powder through powder bed type laser 3D printing.

Nano-LaB ₆ particles (content: 2wt.%), Ti6Al4V alloy powder (content: 25wt.%) and TiAl alloy powder (Al molar content: 48at.%) are mixed in proportions, placed in a ball mill, and pumped into the ball mill. Vacuum and introduce argon gas, and the air pressure is controlled at 0.6MPa; then the mixed powder is subjected to intermittent ball milling, the ball-to-material ratio is 1.5:1, the ball milling speed is 200r/min, and the ball milling time is 4h. At this time, the ball milling input energy and total The number of rotation turns were 2779J/g and 48×10 ³ r respectively; the TiAl-based composite powder finally obtained is shown in Figure 5. The particles still maintain a high sphericity, and the nanoceramic particles are evenly distributed on the surface of the matrix powder;

In the subsequent laser 3D printing process, the laser forming process parameters were optimized as follows: the laser power was 225W, the scanning speed was 300mm/s, the scanning spacing was 100μm, and the powder layer thickness was 50μm. At this time, the volume energy density was 150J/mm. ³ ; The substrate is preheated at 200°C, and the laser scanning strategy is a composite strategy of island scanning + interlayer scanning vector rotation; the side length of the island area is 5mm, and the interlayer rotation angle is 90°. The cross-sectional metallographic photo of the formed sample is shown in Figure 6. It can be seen that there is no obvious crack formation inside the sample, and the sample density is relatively high.

Comparative example 1

The comparative example provided by the present invention uses a TiAl alloy material formed and prepared under the same process parameters as in Example 3. The TiAl alloy material is a TiAl alloy with an Al molar content of 48 at.%. Figure 7 shows the shape of the TiAl alloy powder. appearance, the powder particles show high sphericity;

In the subsequent laser 3D printing process, the laser forming process parameters are as follows: laser power is 225W, scanning speed is 300mm/s, scanning spacing is 100μm, and powder layer thickness is 50μm. At this time, the volume energy density is 150J/mm ³ ; The substrate is preheated at 200°C, and the laser scanning strategy is a composite strategy of island scanning + interlayer scanning vector rotation; the side length of the island area is 5mm, and the interlayer rotation angle is 90°. The cross-sectional metallographic photo of the formed sample is shown in Figure 8. It can be seen that there are obvious microcracks inside the sample, accompanied by some residual pores.

It can be seen from Examples 1-3 of the present invention and Figures 1-6 that with the increase in the amount of Ti6Al4V, the Al molar content in the TiAl alloy material will increase, thereby reducing the dilution effect on the Al content, and Si ₃ N The addition of ₄ promotes the nucleation of a large number of matrix grains, but continuing to increase the use of Si ₃ N ₄ will lead to the deterioration of alloy properties and may lead to an increase in metal corrosion susceptibility.

Comparative Example 1 clearly reflects the effect of nanoceramic particle reinforcement phase in improving TiAl alloy materials, and it can be seen from Examples 1 to 3 and Comparative Example 1 that only under specific ratios and laser parameters , the present invention can achieve the optimal effect.

The TiAl-based composite powder components provided by the invention include nano-ceramic particle reinforcement phase, Ti6Al4V alloy powder dilution phase, and TiAl alloy powder matrix phase, wherein the nano-ceramic particle reinforcement phase is one of Si ₃ N ₄ or LaB ₆ , The selected nanoceramic reinforcement phase can be used as a grain heterogeneous nucleation agent and oxygen scavenger in the high-temperature dynamic melt pool formed by laser. On the one hand, it promotes the nucleation of a large number of matrix grains, helping to achieve columnar crystal orientation, etc. The axial crystal transforms and refines the grains, improving the strength of the matrix.

On the other hand, consuming the dissolved oxygen component in the molten pool through in-situ reaction helps to improve the wettability and bonding strength of the molten channel interface. At the same time, the formed nano-oxide particles can further strengthen the matrix, and its content is controlled at 0.3-2wt.%. , to avoid performance deterioration caused by adding too much; Ti6Al4V alloy powder is added to the matrix powder as a dilute phase to reduce the Al content in the matrix, improve the stability of the β phase with better plasticity in the solidified structure, and reduce the brittleness of the matrix structure. The content is controlled at 15-25wt.% to ensure the dominant position of the TiAl matrix phase.

If the content of Ti6Al4V alloy powder is too low, the dilution effect on the Al content in the TiAl matrix component is not obvious. From the Ti-Al phase diagram, the phase composition of the solidified structure has not changed much, and there is still high crack sensitivity; but the content is too high. , it will lead to a low Al content, a significant reduction in the content of the γ phase with good toughness in the solidified structure, and at the same time, the specific strength and high-temperature properties of the material will also be weakened.

It should be noted that the above embodiments are only used to illustrate the technical solution of the present invention rather than to limit it. Although the present invention has been described in detail with reference to the preferred embodiments, those of ordinary skill in the art should understand that the technical solution of the present invention can be carried out. Modifications or equivalent substitutions without departing from the spirit and scope of the technical solution of the present invention shall be included in the scope of the claims of the present invention.

Claims (10)

1. A TiAl-based lightweight high-temperature material based on laser 3D printing, characterized in that: the TiAl-based lightweight high-temperature material is obtained from TiAl-based composite powder through powder bed type laser 3D printing, wherein the TiAl-based material composite powder The body includes nanoceramic particle reinforcement phase, Ti6Al4V alloy powder dilution phase and TiAl alloy powder matrix phase. 2. The TiAl-based composite powder according to claim 1, characterized in that: the nanoceramic particle reinforced phase content is 0.3-2wt.%, the Ti6Al4V alloy powder diluted phase content is 15-25wt.%, and the rest is TiAl. Alloy powder matrix phase. 3. The TiAl-based composite powder according to claim 1, characterized in that: the nanoceramic particle reinforcement phase is Si ₃ N ₄ or LaB ₆ , the average particle size range is 50 nm, and the purity is above 99.9%. 4. The TiAl-based composite powder according to claim 1, characterized in that: the average particle size range of the diluted phase of the Ti6Al4V alloy powder is 25 μm, the sphericity is >95%, and other elemental impurities are controlled below 0.1wt.%. 5. The TiAl-based composite powder according to claim 1, wherein the TiAl alloy powder matrix phase is a nearly equiatomic titanium-aluminum alloy, in which the mole fraction of Al is between 45 and 48 at.%, and other elemental impurities are present. Control it below 0.1wt.%, the rest is Ti component, the average particle size range is 20-30μm, and the sphericity is >95%. 6. A method for preparing TiAl-based lightweight high-temperature materials based on laser 3D printing according to claim 1, characterized in that: the preparation method includes Mix the nanoceramic particles, Ti6Al4V alloy powder and TiAl alloy powder in proportions, and place them in a ball mill. The ball mill is evacuated and argon gas is introduced, and the air pressure is controlled at 0.4~0.6MPa; then the mixed powder is subjected to intermittent After ball milling, TiAl-based composite powder is obtained, which is then laser formed and solidified. 7. The preparation method according to claim 6, characterized in that: the ball mill adopts a planetary ball mill, the ball milling medium is corundum ceramic balls, the ball milling tank adopts corundum ceramic tank, and the ball-to-material ratio during the ball milling process is 1~ 2.5:1, the ball milling speed is 200~300r/min, and the ball milling time is 2~4h; the ball milling input energy and total rotation number are controlled at 1544~3016J/g and 24~48×10 ³ r respectively. 8. The ball mill input energy according to claim 7, characterized in that: the ball mill input energy E _t where f is the collision frequency, w _d and w _t are the angular velocities of the main disk and tank of the ball mill respectively, E _b is the kinetic energy of the grinding ball, M _p is the powder mass, m _b and v _b are the mass and absolute speed of the grinding ball, R _d and R _t are the gyration radii of the main disk and the tank of the ball mill respectively, r _b and d _b are the radius and diameter of the grinding balls, D _t and H _t are the diameter and height of the tank respectively, N _b is the number of grinding balls numbers, k and ε are constants (equal to 1 and 1.134 respectively); Among them, the total number of rotations λ is the number of rotations of the main disk of the ball mill, λ = nt, where n is the ball milling speed and t is the ball milling time. 9. Laser forming and solidification as claimed in claim 6, characterized in that: it includes: laser forming and solidification of TiAl-based composite powder: mainly including three-dimensional solid modeling, path planning, slicing and layer-by-layer powder spreading and laser scanning solidification process ; Wherein, the thickness of the powder layer involved in the layer-by-layer powder spreading is set to 50 μm; Among them, the laser scanning curing involves main laser process parameter settings including laser power between 150 and 250W, scanning speed between 200 and -600mm/s, and scanning spacing of 100μm; volume energy density is controlled at 133~150J. /mm ³ . 10. The laser scanning curing process as claimed in claim 9, characterized in that: laser scanning curing also involves a laser scanning strategy, here a composite strategy of island scanning + interlayer scanning vector rotation is selected; wherein the side length of the island area is 5~10mm, the inter-layer rotation angle is 45~90°; Among them, laser scanning curing also involves substrate preheating, and the substrate temperature is set at 200°C.