CN116727684A - TiAl-based light high-temperature material based on laser 3D printing and preparation method thereof - Google Patents

TiAl-based light high-temperature material based on laser 3D printing and preparation method thereof Download PDF

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CN116727684A
CN116727684A CN202310482447.6A CN202310482447A CN116727684A CN 116727684 A CN116727684 A CN 116727684A CN 202310482447 A CN202310482447 A CN 202310482447A CN 116727684 A CN116727684 A CN 116727684A
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tial
laser
powder
phase
ball milling
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马成龙
骆伟航
卓焯
武美萍
王全龙
缪小进
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Jiangnan University
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Jiangnan University
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    • B33Y10/00—Processes of additive manufacturing
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    • B33Y70/00—Materials specially adapted for additive manufacturing
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    • C22C32/0005—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with at least one oxide and at least one of carbides, nitrides, borides or silicides as the main non-metallic constituents
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Abstract

The application discloses a TiAl-based light high-temperature material based on laser 3D printing and a preparation method thereof, wherein the TiAl-based composite powder comprises a nano ceramic particle reinforcing phase, a Ti6Al4V alloy powder diluting phase and a TiAl alloy powder matrix phase, wherein the nano ceramic particle reinforcing phase is Si 3 N 4 Or LaB 6 The selected nano ceramic reinforced phase can be used as a grain heterogeneous nucleating agent and an oxygen scavenger in a high-temperature dynamic molten pool formed by laser induction, on one hand, by promoting a large amount of nucleation of matrix grains, the transformation of columnar crystals into equiaxial crystals is facilitated, the grains are thinned, the matrix strength is improved, on the other hand, the oxygen component dissolved in the molten pool is consumed by in-situ reaction, the wettability and the bonding strength of a melt channel interface are improved, and meanwhile, the formed nano oxidized particles can further strengthen the matrix and avoid performance deterioration caused by excessive addition; the Ti6Al4V alloy powder is added into the matrix powder as a diluted phase, so that the stability of a beta phase with better plasticity in a solidification structure is improved, and the brittleness of the matrix structure is reduced.

Description

TiAl-based light high-temperature material based on laser 3D printing and preparation method thereof
Technical Field
The application belongs to the technical field of laser 3D printing, and particularly relates to a TiAl-based light high-temperature material based on laser 3D printing and a preparation method thereof.
Background
The TiAl-based alloy has low density, high melting point, high specific strength and specific stiffness, excellent creep resistance, oxidation resistance, fatigue resistance and the like, is a light high-temperature alloy structural material with excellent performance, has comprehensive performance superior to that of the traditional nickel-based superalloy, and is currently and gradually applied to high-temperature resistant parts in aerospace and vehicle engineering, wings, shells and the like of ultra-high speed aircrafts. However, the low room temperature plasticity and toughness of the TiAl alloy significantly reduce the formability of the TiAl alloy, which severely limits the practical application of the TiAl alloy. Additive manufacturing (or 3D printing) technology has evolved over decades since the germination of the 80 s of the last century, becoming an important component of the current international advanced manufacturing technology front and intelligent manufacturing technology system. As one of the main flows of metal additive manufacturing technology, the powder bed type laser selective area melting technology based on powder layer by layer, line by line scanning and layer by layer melting/solidifying provides a high-efficiency sustainable technical approach for the precise forming of three-dimensional complex components, and can effectively solve the precise forming problem of complex components of difficult-to-process materials such as TiAl alloy.
In the research of TiAl-based alloy laser additive manufacturing, the main difficulty at present is the remarkable crack tendency problem in the forming process. The Ti and Al components form various intermetallic compounds during the laser melting process, such as TiAl and Ti 3 Al、Ti 5 Al 3 And the like, the phases have the characteristics of metal bonds and covalent bonds, have larger hard brittleness and needle-shaped growth morphology, are extremely easy to induce crack formation and expansion, and have more remarkable crack sensitivity particularly in the laser forming process with extremely high temperature gradient and cooling rate. The main methods include optimizing process parameters and raising the preheating temperature of the substrate, however, the improvement effect of the former is limited, the latter often needs to be raised to 800 ℃ and above, a special preheating device needs to be customized, the forming cost is suddenly raised, and meanwhile, serious burning loss of Al element is caused.
Disclosure of Invention
This section is intended to outline some aspects of embodiments of the application and to briefly introduce some preferred embodiments. Some simplifications or omissions may be made in this section as well as in the description of the application and in the title of the application, which may not be used to limit the scope of the application.
The present application has been made in view of the above and/or problems occurring in the prior art.
Therefore, the application aims to overcome the defects in the prior art and provide a TiAl-based light high-temperature material based on laser 3D printing.
In order to solve the technical problems, the application provides the following technical scheme: the TiAl-based light high-temperature material is obtained by forming TiAl-based composite powder through powder bed type laser 3D printing; the TiAl-based composite powder comprises a nano ceramic particle reinforced phase, a Ti6Al4V alloy powder diluted phase and a TiAl alloy powder matrix phase, wherein the addition amount of the nano ceramic particle reinforced phase is within the range of 2 wt%, and the content of the Ti6Al4V alloy powder diluted phase is within the range of 25 wt%; the laser forming process parameters are as follows: the laser power is between 150 and 250W, the scanning speed is between 200 and 375mm/s, the scanning interval is 100 mu m, and the thickness of the powder spreading layer is 50 mu m; the energy density is controlled between 133J/mm and 150J/mm 3 The method comprises the steps of carrying out a first treatment on the surface of the Wherein, energy density η=p/(vdh), where P is laser power, v is scanning speed, d is powder layer thickness, and h is scanning pitch.
As a preferable scheme of the TiAl-based light weight high temperature material of the application, wherein: the content of the reinforcing phase of the nano ceramic particles is 0.3-2 wt%, the content of the diluted phase of the Ti6Al4V alloy powder is 15-25 wt%, and the balance is the TiAl alloy powder matrix phase.
As a preferable scheme of the TiAl-based light weight high temperature material of the application, wherein: the reinforcing phase of the nano ceramic particles is Si 3 N 4 Or LaB 6 The average particle diameter is 50nm, and the purity is more than 99.9%.
As a preferable scheme of the TiAl-based light weight high temperature material of the application, wherein: the average grain diameter range of the diluted phase of the Ti6Al4V alloy powder is 25 mu m, the sphericity is more than 95%, and other element impurities are controlled below 0.1 wt.%.
As a preferable scheme of the TiAl-based light weight high temperature material of the application, wherein: the TiAl alloy powder matrix phase is a near-equiatomic ratio titanium-aluminum alloy, wherein the mole fraction of Al is 45-48 at%, other element impurities are controlled below 0.1 wt%, the balance is Ti component, the average particle size range is 20-30 mu m, and the sphericity is more than 95%.
The application further aims to solve the defects in the prior art and provide a preparation method of the TiAl-based light high-temperature material based on laser 3D printing.
In order to solve the technical problems, the application provides the following technical scheme: a method for preparing the TiAl-based lightweight high temperature material based on laser 3D printing as claimed in claim 1, characterized in that: the preparation method comprises
Mixing nano ceramic particles, ti6Al4V alloy powder and TiAl alloy powder in proportion, placing into a ball mill, vacuumizing the ball mill, and introducing argon, wherein the air pressure is controlled to be 0.4-0.6MPa; and then carrying out intermittent ball milling on the mixed powder to obtain TiAl-based composite powder, and then carrying out laser forming and curing.
As a preferred embodiment of the preparation process according to the application, there is provided: the ball milling adopts a planetary ball mill, the ball milling medium is corundum ceramic balls, a corundum ceramic tank is adopted as a ball milling tank, the ball-material ratio in the ball milling process is 1-2.5:1, the ball milling rotating speed is 200-300 r/min, and the ball milling time is 2-4h; the ball milling input energy and the total rotation number are respectively controlled to be 1544-3016J/g and 24-48 multiplied by 10 3 r。
As a preferred embodiment of the preparation process according to the application, there is provided: the ball milling input energy E t
Where f is the collision frequency, w d And w t Angular velocities of main disc and tank of ball mill, E b Is the kinetic energy of the grinding ball, M p Is the mass of the powder, m b And v b Is the mass and absolute speed of the ball, R d And R is t The radius of gyration of the main disc and the tank body of the ball mill, r b And d b Is the radius and diameter of the grinding ball, D t And H t The diameter and the height of the tank body are respectively N b Is the number of grinding balls, and k and epsilon are constants (equal to 1 and 1.134, respectively);
wherein the total rotation number lambda is the rotation number of the main disc of the ball mill, lambda=nt, n is the ball milling rotation speed, and t is the ball milling time.
As a preferred embodiment of the preparation process according to the application, there is provided: and (3) laser forming and curing of the TiAl-based composite powder: the method mainly comprises three-dimensional solid modeling, path planning, slicing, layer-by-layer powder paving and laser scanning solidification processes;
wherein the layer thickness of the powder spreading layer involved in the layer-by-layer powder spreading is set to be 50 mu m;
wherein, the main laser process parameter setting related to the laser scanning solidification comprises laser power of 150-250W, scanning speed of 200-600 mm/s and scanning interval of 100 μm; the energy density of the energy is controlled between 133J/mm and 150J/mm 3 。
As a preferred embodiment of the preparation process according to the application, there is provided: the laser scanning solidification also relates to a laser scanning strategy, wherein an island scanning and interlayer scanning vector rotation compound strategy is selected; wherein the side length of the island-shaped region is 5-10 mm, and the interlayer rotation angle is 45-90 degrees;
wherein, the laser scanning solidification also involves the preheating of the substrate, and the temperature of the substrate is set at 200 ℃.
The application has the beneficial effects that:
(1) The TiAl-based composite material provided by the application is obtained by forming TiAl-based composite powder through powder bed type laser 3D printing, wherein the optimized powder component design and laser forming process ensure that the final formed part is nearly fully compact and no obvious crack is generated. The TiAl-based composite powder comprises a nano ceramic particle reinforced phase, a Ti6Al4V alloy powder diluted phase and a TiAl alloy powder matrix phase, wherein the nano ceramic particle reinforced phase is Si 3 N 4 Or LaB 6 The selected nano ceramic reinforcing phase can be used as a grain heterogeneous nucleating agent and an oxygen scavenger in a high-temperature dynamic molten pool formed by laser induction, on one hand, by promoting a large amount of nucleation of matrix grains, the transformation of columnar crystal to equiaxial crystal is facilitated, the grains are thinned, the matrix strength is improved, on the other hand, by consuming dissolved oxygen components in the molten pool through in-situ reaction, the wettability and the bonding strength of a melt channel interface are facilitated to be improved, and meanwhile, the formed nano oxidation particles can further strengthen the matrix, the content of the nano oxidation particles is controlled to be 0.3-2wt.%, and the performance deterioration caused by excessive addition is avoided; the Ti6Al4V alloy powder is used as a diluent phase to be added into the matrix powder so as to reduce the content of Al components in the matrix, improve the stability of beta phase with better plasticity in a solidification structure, reduce the brittleness of the matrix structure, and control the content of the beta phase to be 15-25wt.% so as to ensure the main body position of the TiAl matrix phase.
(2) The TiAl-based composite powder is prepared by a mechanical ball milling method, and is different from the traditional single factor regulation and control method, the application provides a comprehensive parameter regulation and control strategy based on the common control of ball milling input energy and total rotation number of a main disc, and the preparation of high-quality composite powder meeting the powder bed type laser 3D printing process is effectively realized, and the obtained composite powder has high sphericity, uniform components, low oxygen content and high powder bed quality.
(3) The laser 3D printing high-performance crack-free TiAl-based composite material provided by the application realizes good forming quality and high density by further optimizing the energy density of laser forming and the laser scanning forming strategy, the functions of the energy density and the scanning forming strategy are realized in the effective regulation and control of multiple physical fields such as a dynamic molten pool temperature field, a solute field, a stress field and the like, the formation of local massive heat accumulation and ultrahigh temperature gradient is avoided, and the formation of thermal cracks can be well inhibited.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present application, the drawings that are needed in the description of the embodiments will be briefly described below, it being obvious that the drawings in the following description are only some embodiments of the present application, and that other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art. Wherein:
FIG. 1 is an SEM photograph of TiAl-based composite powder prepared in example 1 of the present application;
FIG. 2 is a metallographic photograph of a cross section of a sample of a laser 3D printed TiAl-based composite material in example 1 of the present application;
FIG. 3 is an SEM photograph of TiAl-based composite powder prepared in example 2 of the present application;
FIG. 4 is a metallographic photograph of a cross section of a sample of laser 3D printed TiAl-based composite material in example 2 of the present application;
FIG. 5 SEM photograph of TiAl-based composite powder prepared in example 3 of the present application;
FIG. 6 is a metallographic photograph of a cross section of a sample of laser 3D printed TiAl-based composite material in example 3 of the present application;
FIG. 7 is an SEM photograph of TiAl-based alloy powder prepared according to a comparative example of the present application;
fig. 8 is a metallographic photograph of a cross section of a laser 3D printed TiAl-based alloy specimen in comparative example of the present application.
Detailed Description
In order that the above-recited objects, features and advantages of the present application will become more apparent, a more particular description of the application will be rendered by reference to specific embodiments thereof which are illustrated in the appended drawings.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present application, but the present application may be practiced in other ways other than those described herein, and persons skilled in the art will readily appreciate that the present application is not limited to the specific embodiments disclosed below.
Further, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic can be included in at least one implementation of the application. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
Example 1
The application aims to provide a crack-free TiAl-based light high-temperature material based on laser 3D printing, which is obtained by carrying out powder bed type laser 3D printing forming on TiAl-based composite powder
Nano Si 3 N 4 Mixing the particles (content of 0.3 wt.%), ti6Al4V alloy powder (content of 15 wt.%) and TiAl alloy powder (Al molar content of 45 at.%) in proportion, placing into a ball mill, vacuumizing the ball mill, introducing argon gas, and controlling the air pressure at 0.4MPa; then carrying out batch ball milling on the mixed powder, wherein the ball-material ratio is 2.5:1, the ball milling rotating speed is 250r/min, the ball milling time is 2h, and the ball milling input energy and the total rotation number are 3016J/g and 30 multiplied by 10 respectively 3 r; as shown in figure 1, the final TiAl-based composite powder still maintains high sphericity, and meanwhile, the nano ceramic particles are uniformly distributed on the surface of the matrix powder;
in the subsequent laser 3D printing forming process, the laser forming process parameters are optimized as follows: the laser power was 150W, the scanning speed was 200mm/s, the scanning pitch was 100 μm and the thickness of the powder layer was 50. Mu.m, at which time the energy density was 150J/mm 3 The method comprises the steps of carrying out a first treatment on the surface of the The substrate is preheated by 200 ℃, and the laser scanning strategy is an island scanning and interlayer scanning vector rotation composite strategy; wherein the island-shaped region has a side length of 10mm and an interlayer rotation angle of 45 degrees. Formed sampleThe metallographic photograph of the section is shown in fig. 2, and the specimen has no obvious crack formation and relatively high compactness.
Example 2
The application aims to provide a crack-free TiAl-based light high-temperature material based on laser 3D printing, which is obtained by carrying out powder bed type laser 3D printing forming on TiAl-based composite powder
Nano Si 3 N 4 Mixing the particles (content of 0.8 wt.%), ti6Al4V alloy powder (content of 20 wt.%) and TiAl alloy powder (content of 47 at.%) in proportion, placing into a ball mill, vacuumizing the ball mill, introducing argon gas, and controlling the air pressure to be 0.5MPa; then carrying out intermittent ball milling on the mixed powder, wherein the ball-material ratio is 1:1, the ball milling rotating speed is 300r/min, the ball milling time is 2h, and the ball milling input energy and the total rotation number are 2084J/g and 36X 10 respectively at the moment 3 r; as shown in figure 3, the final TiAl-based composite powder still has high sphericity, and the nano ceramic particles are uniformly distributed on the surface of the matrix powder;
in the subsequent laser 3D printing forming process, the laser forming process parameters are optimized as follows: the laser power was 250W, the scanning speed was 375mm/s, the scanning pitch was 100 μm and the laying thickness was 50. Mu.m, at which time the energy density was 133J/mm 3 The method comprises the steps of carrying out a first treatment on the surface of the The substrate is preheated by 200 ℃, and the laser scanning strategy is an island scanning and interlayer scanning vector rotation composite strategy; wherein the island-like region has a side length of 6mm and an interlayer rotation angle of 67 deg.. The metallographic photograph of the section of the formed sample is shown in fig. 4, and the inside of the sample is basically free from crack formation, and the density of the sample is relatively high.
Example 3
The application aims to provide a crack-free TiAl-based light high-temperature material based on laser 3D printing, which is obtained by carrying out powder bed type laser 3D printing forming on TiAl-based composite powder
Nanometer LaB 6 Particles (content 2 wt.%), ti6Al4V alloy powder (content 25 wt.%) and TiAl alloy powder (molar content 48 at.%) were mixed in proportions andplacing the mixture in a ball mill, vacuumizing the ball mill, and introducing argon, wherein the air pressure is controlled to be 0.6MPa; then carrying out batch ball milling on the mixed powder, wherein the ball-material ratio is 1.5:1, the ball milling rotating speed is 200r/min, the ball milling time is 4h, and the input energy and the total rotation number of the ball milling are 2779J/g and 48 multiplied by 10 respectively 3 r; as shown in figure 5, the final TiAl-based composite powder still has high sphericity, and the nano ceramic particles are uniformly distributed on the surface of the matrix powder;
in the subsequent laser 3D printing forming process, the laser forming process parameters are optimized as follows: the laser power was 225W, the scanning speed was 300mm/s, the scanning pitch was 100 μm and the thickness of the powder layer was 50. Mu.m, at which time the energy density was 150J/mm 3 The method comprises the steps of carrying out a first treatment on the surface of the The substrate is preheated by 200 ℃, and the laser scanning strategy is an island scanning and interlayer scanning vector rotation composite strategy; wherein the island-shaped region has a side length of 5mm and an interlayer rotation angle of 90 degrees. The metallographic photograph of the section of the formed sample is shown in fig. 6, and the sample has no obvious crack formation and relatively high density.
Comparative example 1
The comparative example provided by the application adopts TiAl alloy material prepared by forming under the condition of the same technological parameters as the example 3, wherein the TiAl alloy material is TiAl alloy with the Al molar content of 48at percent, and the powder morphology of the TiAl alloy is shown in FIG. 7, and the powder particles show higher sphericity;
in the subsequent laser 3D printing forming process, the laser forming process parameters are as follows: the laser power was 225W, the scanning speed was 300mm/s, the scanning pitch was 100 μm and the thickness of the powder layer was 50. Mu.m, at which time the energy density was 150J/mm 3 The method comprises the steps of carrying out a first treatment on the surface of the The substrate is preheated by 200 ℃, and the laser scanning strategy is an island scanning and interlayer scanning vector rotation composite strategy; wherein the island-shaped region has a side length of 5mm and an interlayer rotation angle of 90 degrees. The cross-sectional metallographic photograph of the formed specimen is shown in FIG. 8, and it can be seen that there are significant microscopic cracks inside the specimen, accompanied by some residual porosity.
As can be seen from examples 1 to 3 and FIGS. 1 to 6 of the present application, the molar content of Al in the TiAl alloy material is increased with the increase of the addition amount of Ti6Al4VWhile reducing the dilution effect on Al content, while Si 3 N 4 The addition of (3) promotes the nucleation of matrix grains in large amounts, but continues to increase Si 3 N 4 The amount of (c) used may lead to deterioration of alloy properties and may lead to an increase in metal corrosion sensitivity.
While comparative example 1 shows the effect of the nano ceramic particle reinforced phase in improving the TiAl alloy material obviously, and as can be seen from examples 1-3 and comparative example 1, the application can achieve the optimal effect only under the specific proportion and laser parameters.
The TiAl-based composite powder provided by the application comprises a nano ceramic particle reinforced phase, a Ti6Al4V alloy powder diluted phase and a TiAl alloy powder matrix phase, wherein the nano ceramic particle reinforced phase is Si 3 N 4 Or LaB 6 On one hand, the selected nano ceramic reinforced phase can be used as a grain heterogeneous nucleating agent and an oxygen scavenger in a high-temperature dynamic molten pool formed by laser induction, so that the transformation of columnar crystals into equiaxed crystals is facilitated by promoting the mass nucleation of matrix grains, the grains are refined, and the matrix strength is improved.
On the other hand, the oxygen component dissolved in the molten pool is consumed through in-situ reaction, so that the wettability and the bonding strength of a melt channel interface are improved, and meanwhile, the formed nano-oxide particles can further strengthen the matrix, the content of the nano-oxide particles is controlled to be 0.3-2wt.%, and the performance deterioration caused by excessive addition is avoided; the Ti6Al4V alloy powder is used as a diluent phase to be added into the matrix powder so as to reduce the content of Al components in the matrix, improve the stability of beta phase with better plasticity in a solidification structure, reduce the brittleness of the matrix structure, and control the content of the beta phase to be 15-25wt.% so as to ensure the main body position of the TiAl matrix phase.
When the content of Ti6Al4V alloy powder is low, the diluting effect on the Al content in the TiAl matrix component is not obvious, and from the aspect of a Ti-Al phase diagram, the phase component of a solidification structure is not changed greatly, and high crack sensitivity still exists; however, if the content is too high, the content of Al is lower, the content of gamma phase with better toughness in a solidification structure is obviously reduced, and meanwhile, the specific strength and high-temperature performance of the material are weakened.
It should be noted that the above embodiments are only for illustrating the technical solution of the present application and not for limiting the same, and although the present application has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that the technical solution of the present application may be modified or substituted without departing from the spirit and scope of the technical solution of the present application, which is intended to be covered in the scope of the claims of the present application.

Claims (10)

1. A TiAl-based light high-temperature material based on laser 3D printing is characterized in that: the TiAl-based light high-temperature material is obtained by forming TiAl-based composite powder through powder bed type laser 3D printing, wherein the TiAl-based composite powder comprises a nano ceramic particle reinforcing phase, a Ti6Al4V alloy powder diluting phase and a TiAl alloy powder matrix phase.
2. The TiAl-based composite powder of claim 1, wherein: the content of the reinforcing phase of the nano ceramic particles is 0.3-2 wt%, the content of the diluted phase of the Ti6Al4V alloy powder is 15-25 wt%, and the balance is the TiAl alloy powder matrix phase.
3. The TiAl-based composite powder of claim 1, wherein: the reinforcing phase of the nano ceramic particles is Si 3 N 4 Or LaB 6 The average particle diameter is 50nm, and the purity is more than 99.9%.
4. The TiAl-based composite powder of claim 1, wherein: the average grain diameter range of the diluted phase of the Ti6Al4V alloy powder is 25 mu m, the sphericity is more than 95%, and other element impurities are controlled below 0.1 wt.%.
5. The TiAl-based composite powder of claim 1, wherein: the TiAl alloy powder matrix phase is a near-equiatomic ratio titanium-aluminum alloy, wherein the mole fraction of Al is 45-48 at%, other element impurities are controlled below 0.1 wt%, the balance is Ti component, the average particle size range is 20-30 mu m, and the sphericity is more than 95%.
6. A method for preparing the TiAl-based lightweight high temperature material based on laser 3D printing as claimed in claim 1, characterized in that: the preparation method comprises
Mixing nano ceramic particles, ti6Al4V alloy powder and TiAl alloy powder in proportion, placing the mixture into a ball mill, vacuumizing the ball mill, and introducing argon, wherein the air pressure is controlled to be 0.4-0.6MPa; and then carrying out intermittent ball milling on the mixed powder to obtain TiAl-based composite powder, and then carrying out laser forming and curing.
7. The method of manufacturing according to claim 6, wherein: the method comprises the steps that a planetary ball mill is adopted for ball milling, a ball milling medium is corundum ceramic balls, a corundum ceramic tank is adopted for a ball milling tank, the ball-material ratio in the ball milling process is 1-2.5:1, the ball milling rotating speed is 200-300 r/min, and the ball milling time is 2-4h; the ball milling input energy and the total rotation number are respectively controlled to be 1544-3016J/g and 24-48 multiplied by 10 3 r。
8. The ball milling input energy of claim 7, wherein: the ball milling input energy E t
Where f is the collision frequency, w d And w t Angular velocities of main disc and tank of ball mill, E b Is the kinetic energy of the grinding ball, M p Is the mass of the powder, m b And v b Is the mass and absolute speed of the ball, R d And R is t The radius of gyration of the main disc and the tank body of the ball mill, r b And d b Is the radius and diameter of the grinding ball, D t And H t The diameter and the height of the tank body are respectively N b Is the number of grinding balls, and k and epsilon are constants (equal to 1 and 1.134, respectively);
wherein the total rotation number lambda is the rotation number of the main disc of the ball mill, lambda=nt, n is the ball milling rotation speed, and t is the ball milling time.
9. The laser formed cure of claim 6, wherein: the method comprises the steps of laser forming and curing of TiAl-based composite powder: the method mainly comprises three-dimensional solid modeling, path planning, slicing, layer-by-layer powder paving and laser scanning solidification processes;
wherein the layer thickness of the powder spreading layer involved in the layer-by-layer powder spreading is set to be 50 mu m;
wherein, the main laser process parameter setting related to the laser scanning solidification comprises laser power of 150-250W, scanning speed of 200-600 mm/s and scanning interval of 100 μm; the energy density of the energy is controlled between 133J/mm and 150J/mm 3 。
10. The laser scanning curing process of claim 9, wherein: the method comprises the steps that laser scanning solidification also relates to a laser scanning strategy, wherein an island scanning and interlayer scanning vector rotation compound strategy is selected; wherein the side length of the island-shaped region is 5-10 mm, and the interlayer rotation angle is 45-90 degrees;
wherein, the laser scanning solidification also involves the preheating of the substrate, and the temperature of the substrate is set at 200 ℃.
CN202310482447.6A 2023-04-30 2023-04-30 TiAl-based light high-temperature material based on laser 3D printing and preparation method thereof Pending CN116727684A (en)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117464022A (en) * 2023-12-28 2024-01-30 西安赛隆增材技术股份有限公司 Additive manufacturing method of gamma-TiAl alloy

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN117464022A (en) * 2023-12-28 2024-01-30 西安赛隆增材技术股份有限公司 Additive manufacturing method of gamma-TiAl alloy
CN117464022B (en) * 2023-12-28 2024-03-29 西安赛隆增材技术股份有限公司 Additive manufacturing method of gamma-TiAl alloy

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