CN114769624B - Device and method for forming TiAl complex metal component by in-situ self-heating effect assisted 3D printing - Google Patents
Device and method for forming TiAl complex metal component by in-situ self-heating effect assisted 3D printing Download PDFInfo
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 202
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 109
- 238000000034 method Methods 0.000 title claims abstract description 74
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 59
- 239000002184 metal Substances 0.000 title claims abstract description 59
- 238000011065 in-situ storage Methods 0.000 title claims abstract description 58
- 230000000694 effects Effects 0.000 title claims abstract description 39
- 238000010146 3D printing Methods 0.000 title claims abstract description 32
- 230000008021 deposition Effects 0.000 claims abstract description 209
- 230000006698 induction Effects 0.000 claims abstract description 107
- 230000008569 process Effects 0.000 claims abstract description 41
- 238000007639 printing Methods 0.000 claims abstract description 28
- 238000005516 engineering process Methods 0.000 claims abstract description 13
- 230000007246 mechanism Effects 0.000 claims abstract description 13
- 238000007648 laser printing Methods 0.000 claims abstract description 8
- 239000000463 material Substances 0.000 claims description 53
- 229910000765 intermetallic Inorganic materials 0.000 claims description 52
- 238000009792 diffusion process Methods 0.000 claims description 36
- 229910052719 titanium Inorganic materials 0.000 claims description 24
- 230000015572 biosynthetic process Effects 0.000 claims description 15
- 238000001816 cooling Methods 0.000 claims description 11
- 239000000843 powder Substances 0.000 claims description 10
- 230000004913 activation Effects 0.000 claims description 8
- 230000001276 controlling effect Effects 0.000 claims description 7
- 238000010891 electric arc Methods 0.000 claims description 7
- 230000001105 regulatory effect Effects 0.000 claims description 6
- 230000001939 inductive effect Effects 0.000 claims description 3
- 230000001737 promoting effect Effects 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 abstract description 20
- 239000000956 alloy Substances 0.000 abstract description 20
- 239000010410 layer Substances 0.000 description 151
- 239000010936 titanium Substances 0.000 description 46
- 230000005674 electromagnetic induction Effects 0.000 description 12
- 229910004349 Ti-Al Inorganic materials 0.000 description 9
- 229910004692 Ti—Al Inorganic materials 0.000 description 9
- 238000006243 chemical reaction Methods 0.000 description 8
- 229910000601 superalloy Inorganic materials 0.000 description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- 238000005495 investment casting Methods 0.000 description 6
- 230000035882 stress Effects 0.000 description 6
- 230000001360 synchronised effect Effects 0.000 description 5
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
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- 238000010521 absorption reaction Methods 0.000 description 2
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- NAWXUBYGYWOOIX-SFHVURJKSA-N (2s)-2-[[4-[2-(2,4-diaminoquinazolin-6-yl)ethyl]benzoyl]amino]-4-methylidenepentanedioic acid Chemical compound C1=CC2=NC(N)=NC(N)=C2C=C1CCC1=CC=C(C(=O)N[C@@H](CC(=C)C(O)=O)C(O)=O)C=C1 NAWXUBYGYWOOIX-SFHVURJKSA-N 0.000 description 1
- 241000251468 Actinopterygii Species 0.000 description 1
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/25—Direct deposition of metal particles, e.g. direct metal deposition [DMD] or laser engineered net shaping [LENS]
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
- B22F10/364—Process control of energy beam parameters for post-heating, e.g. remelting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
- B22F10/366—Scanning parameters, e.g. hatch distance or scanning strategy
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/50—Treatment of workpieces or articles during build-up, e.g. treatments applied to fused layers during build-up
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/80—Data acquisition or data processing
- B22F10/85—Data acquisition or data processing for controlling or regulating additive manufacturing processes
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y30/00—Apparatus for additive manufacturing; Details thereof or accessories therefor
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
- B33Y40/20—Post-treatment, e.g. curing, coating or polishing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y50/00—Data acquisition or data processing for additive manufacturing
- B33Y50/02—Data acquisition or data processing for additive manufacturing for controlling or regulating additive manufacturing processes
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y80/00—Products made by additive manufacturing
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- Powder Metallurgy (AREA)
Abstract
The invention discloses a device and a method for forming a TiAl complex metal component by in-situ self-heating effect assisted 3D printing. The device comprises LDED forming equipment and arc induction heating equipment; LDED the forming equipment comprises a LDED control device, a printing platform and a laser printing deposition head, wherein the laser printing deposition head can deposit on the printing platform to form a deposition body according to a preset printing path in the LDED control device under the control of the LDED control device; the arc induction heating apparatus includes a lifting mechanism, an arc induction coil, and an induction relay, the arc induction coil being disposed outside a contour of the deposition body. When the method is used for forming the TiAl complex metal component by adopting LDED technology, an in-situ self-heating effect treatment process is assisted to improve the service performance of the integral component, and the TiAl alloy component with a complex structure is formed in a high-quality, high-precision, defect-free and homogenizing way.
Description
Technical Field
The invention belongs to the technical field of 3D printing and forming of metal components, and particularly relates to a device and a method for forming a TiAl complex metal component by in-situ self-heating effect assisted 3D printing.
Background
TiAl alloy has unique comprehensive properties (high specific stiffness, elastic modulus and density ratio), and TiAl, ti 3 Al and the like are new generation high-performance structural materials. They have low density, high temperature strength, high melting point and excellent creep resistance, oxidation resistance and high specific stiffness properties, which make them widely used in the field of aerospace structures. Compared with the traditional nickel-based superalloy and titanium alloy, the TiAl alloy has the following density: the density of the TiAl alloy (3.5 g/cm 3) is about half that of the nickel-base superalloy (8.3 g/cm 3); mechanical properties at room temperature: the specific stiffness (150 GPa) of TiAl alloy is higher than that of titanium alloy (110 GPa), but lower than that of nickel-based superalloy (206 GPa); high temperature mechanical properties: the creep limit (1000 ℃) and oxidation limit (1000 ℃) of TiAl alloys are higher than those of titanium alloys (600 ℃ and 600 ℃ oxidation limit), but slightly lower than those of nickel-base superalloys (1093 ℃ and 1093 ℃ oxidation limit). It follows that while TiAl alloys are somewhat inferior to nickel-base superalloys, tiAl alloys have significantly lower density than nickel-base superalloys and comparable specific stiffness to nickel-base superalloys. Therefore, the TiAl alloy is expected to replace the existing nickel-based superalloy system and has wide application prospect in the aviation industry and the automobile industry, and the TiAl alloy is considered to be the first-choice material of the static piece and the rotating piece of the novel aerospace engine, such as a nozzle adjusting fish scale, a high-pressure compressor guide blade, a piston cover and the like.
The traditional forming method of TiAl alloy mainly comprises precision casting, powder metallurgy and the like. Two main categories are involved for precision casting: one type is investment casting, and the other type is metal die casting. Investment casting is mainly used for forming TiAl alloy components with relatively complex shapes; and metal mold casting is mainly used for producing components with relatively regular shapes and relatively large yields. The precision casting method forming member mainly has the advantages of low cost, easy forming and the like; however, serious casting defects (such as air holes, looseness and the like) exist in the casting process, and the components are easily cracked in the cooling process, so that the mechanical properties of the components, particularly the ductility of the components at room temperature, are greatly reduced. Investment casting, while it is possible to form relatively complex structural members, it is difficult to achieve integral forming with sharp corners or thin wall structures.
Powder metallurgy is another common method of forming TiAl alloy components. Powder metallurgy can avoid problems such as component segregation, coarse grains, and uneven structure that occur in casting, thereby improving ductility of the TiAl alloy member at room temperature. However, the addition of binders during powder metallurgy results in difficult control of interstitial element composition and microstructure and phase, which limits the use of this process.
3D printing techniques can efficiently integrate complex metal components. Because the 3D printing technology is different from the traditional material reduction and equal material forming method, the 3D printing utilizes high-energy beam to quickly melt and solidify metal powder, the two-dimensional section of the periodic fused component is formed into a three-dimensional component through metallurgical bonding along the forming direction, and the integrated forming of the complex component can be met to the maximum extent based on the three-dimensional-two-dimensional-three-dimensional forming principle. 3D printing can thus produce essentially any complex structure of components.
Although the TiAl alloy member with a complex structure can be formed by the existing 3D printing technology (laser directional energy deposition, abbreviated as LDED), on one hand, cracks are easy to initiate at the interface position of the TiAl alloy 3D printing forming member in the forming manufacturing process due to the rapid heating and rapid cooling of the LDED forming process, on the other hand, uneven distribution of intermetallic compounds of the TiAl alloy 3D printing forming member is easy to be caused, and when the TiAl alloy 3D printing forming member bears load, uneven distribution of internal stress of the material is caused due to the existence of the intermetallic compounds between the interface and the TiAl, so that initiation and expansion of the cracks are caused, and the service period of the member is greatly reduced.
Disclosure of Invention
The invention aims to: the invention aims to solve the problems of the prior LDED forming and manufacturing, in particular to a device and a method for forming a TiAl complex metal component by in-situ self-heating effect assisted 3D printing, which are assisted by an in-situ thermal effect process in the 3D printing (LDED) forming process to drive chemical components (Ti and Al) of the 3D printing and forming component to diffuse and react at a 3D printing interface to form intermetallic compounds, so that the TiAl alloy component with a complex structure can be finally formed with high quality, high precision, no defects and homogenization.
In order to achieve the technical purpose, the invention adopts the following technical scheme:
An in-situ self-heating effect assisted 3D printing device for forming TiAl complex metal components comprises LDED forming equipment and arc induction heating equipment; the LDED forming equipment comprises a LDED control device, a printing platform and a laser printing deposition head, wherein the laser printing deposition head can deposit on the printing platform to form a deposition body according to a printing path preset in the LDED control device under the control of the LDED control device, and the deposition body comprises alternately laminated Ti deposition layers, al deposition layers and interface layers between the Ti deposition layers and the Al deposition layers; the electric arc induction heating equipment comprises a lifting mechanism, an electric arc induction coil and an induction relay;
The arc induction coil is arranged outside the outline of the deposition body, is connected with a power supply after being connected with the induction relay in series, is connected with the power output end of the lifting mechanism, and can drive the arc induction coil to lift relative to the printing platform under the control of the LDED control device;
After each deposition layer of the deposition body deposits N deposition layers, synchronously carrying out induction heating on the part with the height H in the deposited N deposition layers by controlling a lifting mechanism; wherein:
H＝HN-n
Wherein: h N represents the total height of the N layers deposited, N is more than or equal to 1; n represents a heat affected zone size parameter.
Preferably, the arc induction coil is a spiral heating coil; the spiral heating coil comprises a plurality of layers of heating coils, and each layer of heating coil is provided with an induction relay;
Each heating coil corresponds to one deposition layer of the deposition body;
The LDED control device can dynamically turn on or off the corresponding induction relay on the spiral heating coil according to the deposition speed of each layer of deposition layer in the deposition body.
Preferably, the LDED control device can determine the moving speed v r of the spiral heating coil driven by the lifting mechanism and the heating time t of each layer of heating coil according to the laser scanning speed v 1 and the induction heating time tau required by the deposition body formed by the N layers of deposition layers.
Preferably, the moving speed v r of the spiral heating coil satisfies:
in the above formula, C represents the number of layers of a deposition layer requiring induction heat treatment in a deposition body; k 1,k2,k3 represents the speed scaling factor under different deposition layer number ranges, and x i is the deposition layer thickness.
Preferably, the number of turns ω of the heating coil required for the deposition body made up of N deposition layers is:
ω＝ΔIω×H/I
wherein: Δi ω represents ampere turns per unit length of the heating coil, and H represents the height of a portion to be induction-heated in the deposited body made up of N deposited layers; i represents the current of the heating coil.
Preferably, the current I of the heating coil is:
Electric power P Q of induction heating coil:
induction heat Q required for a deposition body made of N deposition layers:
Q＝M×θ×(Tm-T0)
wherein: u represents the potential amplitude of the power supply; Representing an electric power factor; η represents the thermal efficiency; τ represents the induction heating time required for a deposition body made up of N deposition layers; m represents the mass of a deposition body formed by N deposition layers; θ represents the specific heat capacity of the deposit; t m represents the temperature of a deposition body formed by N deposition layers after being heated by an induction heating coil; t 0 denotes the ambient temperature.
Preferably, the temperature T m of the deposition body formed by the N deposition layers after being heated by the induction heating coil is as follows:
H2＝k′1τk
Wherein: h represents the thickness of a deposition body formed by N deposition layers, which is required to be subjected to induction heating; k is a material property correlation constant; d is a diffusion coefficient; τ k is the diffusion time; k' 1 is the diffusion layer growth coefficient; k is a constant; q n is diffusion activation energy; r is a gas constant; t m is the temperature of the deposition body formed by the N deposition layers after being heated by the induction heating coil.
Preferably, the LDED control device can be controlled by regulating the laser power P, the laser scanning rate v 1 and the cooling rate v 2.
Another technical object of the present invention is to provide a method for forming a TiAl complex metal member by in-situ self-heating effect assisted 3D printing, which is realized based on the above-mentioned apparatus for forming a TiAl complex metal member by in-situ self-heating effect assisted 3D printing, comprising the steps of:
step one, printing and forming a deposition body with preset thickness by adopting LDED forming process
Based on LDED forming equipment, adopting LDED forming technology, and alternately printing and forming Ti and Al metal powder according to a preset printing path to obtain a deposit body with preset thickness;
The deposition body comprises a laminated Ti deposition layer and an Al deposition layer, and an interface layer positioned at the interface joint of the Ti deposition layer and the Al deposition layer;
In the printing forming process of the deposition body, forming TiAl intermetallic compounds wrapped between the Ti deposition layer and the Al deposition layer in the interface layer by regulating and controlling the technological parameters of LDED forming technology so as to inhibit the formation of cracks of the TiAl intermetallic compounds;
step two, promoting formation of TiAl intermetallic compounds in a sediment interface layer by an in-situ heat post-treatment process
Based on arc induction heating equipment, the deposition body obtained in the step one is subjected to induction heat treatment by adopting an in-situ heat post-treatment process so as to drive metal Ti atoms of the Ti deposition layer to diffuse towards the interface layer after being separated from the binding, and metal Al atoms of the Al deposition layer to diffuse towards the interface layer after being separated from the binding, thereby inducing the TiAl intermetallic compound formed in the interface layer to grow gradually so as to promote the formation of the TiAl intermetallic compound and lead the TiAl intermetallic compound between the Ti deposition layer and the Al deposition layer to be uniform.
Preferably, in the first step, during the printing forming process of the deposition body, the process parameters of the molding process of LDED are regulated and controlled to include laser power P, laser scanning rate v 1 and cooling rate v 2; in the second step, the moving speed v r of the spiral heating coil driven by the lifting mechanism and the heating time t of each layer of heating coil are determined according to the laser scanning speed v 1 and the induction heating time tau required by the deposition body formed by the N layers of deposition layers.
Based on the technical scheme, compared with the prior art, the invention has the following advantages:
(1) The invention adopts LDED technology and in-situ heat treatment composite technology to realize the integral formation of the complex structure of the TiAl material with high defect tendency; meanwhile, product customization can be realized according to production requirements, and the delivery period is shortened. The component yield and the component complexity can be improved compared with the traditional processing method. Therefore, has better economic value.
(2) The invention adopts an in-situ self-heating effect method to synchronously heat treat the deposited metal layer. The thermal expansion coefficients of pure Ti (8.6X10 -6/K) and pure Al (23X 10 -6/K) and the Poisson ratios of Ti, al and TiAl are respectively 0.34, 0.25 and 0.24, so that the volume expansion rate of Al in the forming process is higher, microscopic cracks are easy to appear on the TiAl interface, and the mechanical property of the material is obviously reduced; meanwhile, because of the difference of plastic deformation capability in the heterogeneous material bearing process, microscopic cracks are easy to appear on the side of the material with poor plasticity. By adopting an in-situ dynamic heat treatment scheme, the heated tungsten wire dynamically acts on the pure Ti and pure Al areas to promote the continuous diffusion reaction between atoms to produce TiAl intermetallic compounds. The process can effectively eliminate plastic deformation and micro cracks of the material caused by the difference of thermal physical parameters, and simultaneously, the uniform TiAl intermetallic compound formed under the compound effect of LDED and in-situ heat treatment can effectively improve the mechanical property of the whole metal component.
(3) According to the invention, the spiral heating tungsten wire is added on the substrate, so that the material is subjected to heat treatment synchronously in the laser processing and forming process. This greatly reduces the forming time of the single metal component, reducing the time cost.
(4) The invention designs an induction heating spiral heating tungsten wire, and an induction relay is arranged on each tungsten wire layer. When the deposition of a layer of material is completed, the induction relay receives the signal and converts the thermal signal into an electrical signal, which is transmitted to the induction heating coil, and the tungsten wire harvests the signal for induction heating. Finally, the aim of inductively heating a layer of material is fulfilled after each layer of material is deposited.
Drawings
FIG. 1 is an in situ self-heating effect based thermal processing apparatus according to the present invention;
FIG. 2 is a Ti-Al phase diagram of a printed TiAl complex metal component of the present invention;
FIG. 3 is a particle size distribution of a specialty metal powder useful in the present invention;
FIG. 4a is a Ti-Al interface microstructure of a slice of a TiAl complex metal member under an optical microscope obtained by adopting the prior LDED forming technology, and FIG. 4b is a Ti-Al interface microstructure of a slice of a TiAl complex metal member under an optical microscope obtained by adopting the method of the invention;
FIG. 5a is a Ti-Al interface microstructure of LDED formed TiAl complex metal member slice under a scanning electron microscope, and FIG. 5b is a Ti-Al interface microstructure of TiAl complex metal member slice under a scanning electron microscope obtained by the method of the invention;
fig. 6a and 6b correspond to the areas and diffraction patterns of a transmission electron microscope under a scanning electron microscope of a slice of a TiAl complex metal component obtained by the method according to the invention.
Fig. 7 is a flow chart of the method of the present invention.
FIGS. 8a-e respectively show the heat affected zone n of a TiAl alloy component with different deposited layers.
Detailed Description
The following description of the embodiments of the present invention will be made clearly and completely with reference to the accompanying drawings, in which it is apparent that the embodiments described are only some embodiments of the present invention, but not all embodiments. The following description of at least one exemplary embodiment is merely exemplary in nature and is in no way intended to limit the invention, its application, or uses. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention. The relative arrangement, expressions and numerical values of the components and steps set forth in these embodiments do not limit the scope of the present invention unless it is specifically stated otherwise. Techniques, methods, and apparatus known to one of ordinary skill in the relevant art may not be discussed in detail, but should be considered part of the specification where appropriate. In all examples shown and discussed herein, any specific values should be construed as merely illustrative, and not a limitation. Thus, other examples of the exemplary embodiments may have different values.
The invention improves the performance of the TiAl complex metal component obtained by the existing LDED forming technology by changing the interface structure of the TiAl complex metal component obtained by the existing LDED forming technology. For this purpose, the invention drives the chemical components (Ti, al) of the 3D printing forming member to diffuse and react at the 3D printing interface through an in-situ thermal effect auxiliary process in LDED forming process. Specifically, based on the existing LDED forming equipment, an in-situ heat treatment equipment (an electric arc induction heating equipment, the structure of which is shown in fig. 1) based on self-heating effect is arranged, and a control device of the existing LDED forming equipment is adjusted, so that the in-situ heat treatment equipment performs in-situ induction heat treatment after the LDED forming equipment completes a deposition body with a certain thickness (formed by alternately stacking Ti deposition layers and Al deposition layers), and the aim of synchronous treatment of three-dimensional deposition and in-situ self-heating effect of a component is achieved.
Therefore, the device for forming the TiAl complex metal component by in-situ self-heating effect assisted 3D printing comprises LDED forming equipment and arc induction heating equipment; wherein:
The LDED forming equipment comprises a LDED control device, a printing platform and a laser printing deposition head, wherein the laser printing deposition head can deposit on the printing platform to form a deposition body according to a preset printing path in the LDED control device under the control of the LDED control device, and the deposition body comprises alternately laminated Ti deposition layers, al deposition layers and interface layers between the Ti deposition layers and the Al deposition layers.
The electric arc induction heating equipment comprises a lifting mechanism, an electric arc induction coil and an induction relay;
The arc induction coil is arranged outside the outline of the deposition body, is connected with a power supply after being connected with the induction relay in series, is connected with the power output end of the lifting mechanism, and can drive the arc induction coil to lift relative to the printing platform under the control of the LDED control device;
After each deposition layer of the deposition body deposits N deposition layers, synchronously carrying out induction heating on the part with the height H in the deposited N deposition layers by controlling a lifting mechanism; wherein:
H＝HN-n
Wherein: h N represents the total height of the N layers deposited, N is more than or equal to 1; n represents a heat affected zone size parameter.
Preferably, the arc induction coil is a spiral heating coil; the spiral heating coil comprises a plurality of layers of heating coils, and each layer of heating coil is provided with an induction relay; each heating coil corresponds to one deposition layer of the deposition body; the LDED control device can dynamically turn on or off the corresponding induction relay on the spiral heating coil according to the deposition speed of each layer of deposition layer in the deposition body.
Preferably, the LDED control device can determine the moving speed v r of the spiral heating coil driven by the lifting mechanism and the heating time t of each layer of heating coil according to the laser scanning speed v 1 and the induction heating time tau required by the deposition body formed by the N layers of deposition layers.
Preferably, the moving speed v r of the spiral heating coil satisfies:
in the above formula, C represents the number of layers of a deposition layer requiring induction heat treatment in a deposition body; k 1,k2,k3 represents the speed scaling factor under different deposition layer number ranges, and x i is the deposition layer thickness.
Preferably, the number of turns ω of the heating coil required for the deposition body made up of N deposition layers is:
ω＝ΔIω×H/I
wherein: Δi ω represents ampere turns per unit length of the heating coil, and H represents the height of a portion to be induction-heated in the deposited body made up of N deposited layers; i represents the current of the heating coil.
Preferably, the current I of the heating coil is:
Electric power P Q of induction heating coil:
induction heat Q required for a deposition body made of N deposition layers:
Q＝M×θ×(Tm-T0)
wherein: u represents the potential amplitude of the power supply; Representing an electric power factor; η represents the thermal efficiency; τ represents the induction heating time required for a deposition body made up of N deposition layers; m represents the mass of a deposition body formed by N deposition layers; θ represents the specific heat capacity of the deposit; t m represents the temperature of a deposition body formed by N deposition layers after being heated by an induction heating coil; t 0 denotes the ambient temperature.
Preferably, the temperature T m of the deposition body formed by the N deposition layers after being heated by the induction heating coil is as follows:
H2＝k′1τk
Wherein: h represents the thickness of a deposition body formed by N deposition layers, which is required to be subjected to induction heating; k is a material property correlation constant; d is a diffusion coefficient; τ k is the diffusion time; k' 1 is the diffusion layer growth coefficient; k is a constant; q n is diffusion activation energy; r is a gas constant; t m is the temperature of the deposition body formed by the N deposition layers after being heated by the induction heating coil.
Preferably, the LDED control device can be controlled by regulating the laser power P, the laser scanning rate v 1 and the cooling rate v 2.
The invention provides a device for forming a TiAl complex metal component by in-situ self-heating effect assisted 3D printing, which is based on the device, and provides a method for forming the TiAl complex metal component by in-situ self-heating effect assisted 3D printing, as shown in FIG. 8, and the method comprises the following steps:
step one, printing and forming a deposition body with preset thickness by adopting LDED forming process
Adopting LDED forming process, and alternately printing and forming Ti and Al metal powder according to a preset printing path to obtain a deposit body with preset thickness;
The deposition body comprises a laminated Ti deposition layer and an Al deposition layer, and an interface layer positioned at the interface joint of the Ti deposition layer and the Al deposition layer;
In the printing forming process of the deposition body, forming TiAl intermetallic compounds wrapped between the Ti deposition layer and the Al deposition layer in the interface layer by regulating and controlling the technological parameters of LDED forming technology so as to inhibit the formation of cracks of the TiAl intermetallic compounds; specifically, the laser power P, the scanning speed v 1, the powder feeding quantity delta and the material cooling speed v 2 of the LDED forming process are selected by researching the temperature of a TiAl intermetallic compound phase region in a TiAl alloy phase diagram, so that a TiAl intermetallic compound wrapped between a Ti deposition layer and an Al deposition layer is formed in an interface layer, and the formation of cracks of the TiAl intermetallic compound is inhibited.
Step two, promoting formation of TiAl intermetallic compounds in a sediment interface layer by an in-situ heat post-treatment process
And (3) carrying out induction heat treatment on the deposition body obtained in the step one by adopting an in-situ heat post-treatment process (mainly an in-situ induction heat treatment process) so as to drive metal Ti atoms of the Ti deposition layer to diffuse towards the interface layer after being separated from the binding and metal Al atoms of the Al deposition layer to diffuse towards the interface layer after being separated from the binding, thereby inducing the TiAl intermetallic compound formed in the interface layer to grow gradually so as to promote the formation of the TiAl intermetallic compound and lead the TiAl intermetallic compound between the Ti deposition layer and the Al deposition layer to be uniform.
The in-situ induction heat treatment process is realized by an in-situ induction heat treatment device (arc induction heating device), and a key component of the arc induction heating device is the design of an induction heating coil. The present invention is directed to the forming member dimensions (volume V of material, surface area S, and mass M of material), structural shape and thermal driving temperature (based on surface unit power Δp s when material is heated and material heating absorption heat Q to complete the conversion of material required absorption heat to electric power P Q of induction heating coil) and destressing annealing temperature T to complete the in-situ heating coil design (current I of heating coil, number of heating coil turns ω required for the deposition body of N layers of deposition layer required to be reached in induction heating coil). In the forming process of the member LDED, the coil can judge the moving speed v r of the induction heating coil according to the scanning speed v 1, the deposition speed v c and the time tau of the material needing heat treatment in the laser forming process, so that the forming of the material and the in-situ heat treatment of the material can be synchronously performed; meanwhile, the coil is digitally driven to synchronously move according to the space deposition speed of the component, so that the whole heat treatment process of the material can be automatically finished. After in-situ heat treatment, the material is made into TiAl intermetallic compound, so that the service performance of the integral member is improved.
LDED the forming equipment alternately deposits and forms the powder of the Ti and the Al. By adjusting the forming process parameters of laser power P, laser scanning speed v 1 and cooling speed v 2, tiAl metal compounds are stably generated on the interface when the TiAl metal component is formed. Specifically, by observing the stable phase region of the TiAl intermetallic compound in the TiAl phase diagram (shown in fig. 2), the cooling rate v 2 of the material is further judged, and the laser power P and the scanning rate v 1 are controlled to cool the phase region of the TiAl intermetallic compound in the material deposition forming process, so that the purpose of obtaining the TiAl intermetallic compound in the component three-dimensional deposition forming process is achieved. The deposition thicknesses of the Ti and Al layers were recorded simultaneously as h 1 and h 2, respectively. In the second step, the heat treatment temperature required to be reached by the in-situ self-heating effect of the forming component is calculated to be T m; the ambient temperature is T 0. The outer diameter of the deposition cylinder member is D w, the inner diameter is D n, the overall height of the member is H 1, and the specific heat capacity of the member material is recorded as theta. Thus, the volume of material heated is:
The surface area of the material after heating is noted as:
The mass of the component is recorded as follows:
Where γ is the heating material density.
The heat required to be absorbed by the material when the material is subjected to in-situ heat treatment is as follows:
Q＝M×θ×(Tm-T0) (4)
the heat required after the heating of the component is converted into electric power of the induction heating coil:
Where η is the thermal efficiency (the heating efficiency may be 0.8) at the time of heating, and τ is the time required for heating.
The current of the heating coil is:
In the above For supplying the electric power factor (the electric power factor can take a value of 0.8).
The surface area unit power of the heated member is:
ΔPs＝PQ×1000/S (7)
We therefore calculated the number of heating coil turns required for a deposit of N deposited layers as:
ω＝ΔIω×H/I (8)
Δi ω in the above formula is ampere-turns of unit length, and can be obtained according to the curve relationship between Δp s and Δi ω.
And after the formation of the component is finished, performing post-treatment on the metal component by using a designed in-situ self-heating effect heat treatment device. An induction relay is arranged on the arc induction heater, and after N layers of Ti or Al materials ts are deposited according to LDED, the previous N-N (N is a heat affected zone size parameter) deposition layers are synchronously subjected to induction heating.
The heat of the deposited Ti or Al layer is transferred to the depth direction, so that the heat affected zone of the deposited Ti or Al layer is enlarged. Therefore, the temperature of the later deposited layer is higher than that of the earlier deposited layer and the temperature tends to be stable when a certain number of layers are deposited. In order to achieve the synchronous treatment target of the three-dimensional deposition and the in-situ self-heating effect of the component, the induction heater synchronously moves along the Z direction along with the deposition rate so as to realize the dynamic synchronous heat treatment target of the component. Therefore, when the electromagnetic induction heating coil heats the prior deposition layer, the moving speed v r of the electromagnetic induction heating coil is slower because the heat affected zone is smaller and the temperature is lower and the heating time is longer; and then the heating time required by the higher temperature of the deposited layer is shorter than that of the deposited layer before the deposited layer is heated because of larger heat affected zone, and the moving speed v r of the electromagnetic induction heating coil is faster. Specifically, the moving speed v r is:
In the above formula, k 1,k2,k3 is the speed proportionality coefficient in the range of 0 < C.ltoreq.2, 3.ltoreq.C.ltoreq.4 and C.ltoreq.5 of the deposition layer respectively, and x i is the thickness of the deposition layer.
Finally, a TiAl compound homogenization process generated by LDED forming member deposition interface and thermal diffusion reaction is realized, namely, the metal members are TiAl intermetallic compounds. The integrally formed metal member has excellent mechanical properties thanks to the excellent material properties of the TiAl intermetallic compound.
As a preferred embodiment of the present invention, the cooling rate v 2 is obtained by controlling the laser power P at the time of laser scanning, the laser scanning rate v 1, and the phase region where the TiAl intermetallic compound exists observed through the TiAl phase diagram to estimate, thereby achieving effective regulation of formation of the TiAl intermetallic compound.
As a preferred embodiment of the present invention, during the forming process, we use the in-situ self-heating effect to heat treat the formed metal member to achieve the continuous diffusion and reaction of Ti and Al atoms to form the TiAl intermetallic compound, so as to achieve the purpose of homogenizing the TiAl intermetallic compound.
As a preferred embodiment of the invention, the in-situ heat treatment device is dynamically synchronized with the formation of the metal member based on an arc induction in-situ dynamic heating method by placing the induction heating device outside the pre-deposition body profile and then forming the member according to LDED the Z-deposition rate v c and the heat-affected zone size n.
As a preferred embodiment of the present invention, an induction relay is installed on the heating coil of each layer, so that the induction relay can dynamically turn off/on the heat treatment according to the material deposition rate, and the heating time t of the coil and the coil moving rate v r can be determined according to the laser scanning rate v 1, the metal member heat treatment time τ.
As a preferred embodiment of the invention, when the TiAl intermetallic compound is formed by laser additive manufacturing, tiny cracks exist at interfaces of different deposition layers in the forming process due to the difference between the elastic modulus and the thermal expansion coefficient of the TiAl intermetallic compound and pure Ti and pure Al (the elastic modulus and the thermal expansion coefficient of pure Ti are respectively 106.4GPa and 8.6X10 -6/K, and the elastic modulus and the thermal expansion coefficient of pure Al are respectively 70GPa and 23X 10 -6/K). However, the LDED deposition process in-situ self-heating effect method provided by the invention: (1) The thermal stress and the volume change stress of the TiAl intermetallic compound formed at the Ti and Al interface in the LDED deposition process are wrapped by Ti and Al materials with excellent plasticity, and (2) the in-situ self-heating effect is combined with LDED forming heat affected zone effect, so that the diffusion of Ti and Al atoms can be promoted, the residual stress and the cracking tendency can be reduced, and the aim of homogenizing the whole material is finally realized.
The thickness of the reaction diffusion layer of the component is related to the electromagnetic induction heating time and the heating temperature. The Gibbs free energy G of the component gradually increases along with the rise of the temperature; when the Gibbs free energy G exceeds the energy barrier (i.e. diffusion activation energy Q n) needed to be crossed by the atomic motion, ti and Al atoms are separated from the constraint among the atoms, so that the atoms in the Ti and Al deposition layers are mutually reacted and diffused, and the purpose of expanding the phase region of the TiAl intermetallic compound is achieved. The thickness of the diffusion reaction layer and the diffusion time are parabolic:
x2＝k′1τk (11)
In the above formula, x is the thickness of the diffusion layer; k is a material property correlation constant; d is a diffusion coefficient; τ k is the diffusion time; k' 1 is the diffusion layer growth coefficient; k is a constant; q n is diffusion activation energy; r is a gas constant; t m is the temperature of the deposition body formed by the N deposition layers after being heated by the induction heating coil.
Fig. 4a is a Ti-Al interface microstructure of a slice of a TiAl complex metal component under an optical microscope obtained by using the existing LDED forming technique, and fig. 4b is a Ti-Al interface microstructure of a slice of a TiAl complex metal component under an optical microscope obtained by using the method of the present invention. By analysis, microscopic cracks still can be generated at a TiAl deposition interface due to rapid heating and rapid cooling in LDED forming processes before the materials do not perform in-situ self-heating effect, and after the in-situ self-heating effect interacts with a heat affected zone in LDED forming, tiAl intermetallic compounds are wrapped by Ti and Al materials with excellent plasticity, so that the internal stress and deformation of the TiAl intermetallic compounds under LDED forming cycle heat treatment are absorbed by the Ti and Al materials, and the formation of the TiAl intermetallic compound cracks is inhibited.
FIG. 5a is a Ti-Al interface microstructure of LDED formed TiAl complex metal member slice under a scanning electron microscope, and FIG. 5b is a Ti-Al interface microstructure of TiAl complex metal member slice under a scanning electron microscope obtained by the method of the invention;
Fig. 6a and 6b correspond to the areas and diffraction patterns of a transmission electron microscope under a scanning electron microscope of a slice of a TiAl complex metal component obtained by the method according to the invention. After the component interacts with LDED forming heat affected zone through in-situ self-heating effect, tiAl intermetallic compound zone grows up gradually. The growing intermetallic compound can be judged to be TiAl intermetallic compound by analyzing the long and large area through a transmission electron microscope.
Application example
The two-dimensional cross section of the periodic fused member is metallurgically bonded together in the forming direction to form a three-dimensional member by rapidly melting and solidifying the metal powder with a high energy beam using raw Ti and Al powders of 40 to 80 μm in size. The laser scanning speed of the laser is 3mm/s, the laser power is 2000W, and the powder feeding amount is 10r/min. The forming member had a dimension of inner diameter D n mm, outer diameter D w of 170mm, wall thickness of 10mm and height H 1 of 205mm.
The component volume and surface area were calculated from the above formulas (1), (2).
LDED forming the finished component, and performing post-treatment on the metal component by using a heat treatment device with an in-situ self-heating effect, wherein the heat treatment temperature is 650 ℃, the temperature is recorded as T m, and the heating time is tau. And an induction relay is arranged on the arc induction coil, and after each N-layer material t s is deposited, the previous N-N (N is the size parameter of the heat affected zone) deposition layer is synchronously subjected to induction heating so as to achieve the aim of synchronous treatment of three-dimensional deposition and in-situ self-heating effect of the component. The thermal efficiency was taken to be 0.8, and the number of turns ω of the heating coil required for the deposition body constituted by N deposition layers was calculated. The calculation means is required to achieve the required amount of absorbed heat Q for homogenization and to convert the required amount of heat Q into the electric power P Q of the induction heating coil (calculated by the above formula 3). The unit length ampere-turn delta I ω of the electromagnetic induction coil is determined by calculating the electric power P Q of the induction heating coil which is required to be consumed when the material is heated to the required temperature, calculating the current I of the heating coil and the unit surface area power delta P s and determining the relation curve between the unit length ampere-turn delta I ω and the unit surface area power delta P s. The number of turns of the electromagnetic induction coil is calculated from the above equation (8).
According to the simulation result, the range of the heat affected zone in the number of layers C of the deposition body of different deposition layers needing induction heat treatment is determined. The ranges of different heat affected zones of the formed component, the number of layers C of the deposited layers in the deposited body requiring induction heat treatment and the moving speed v r of the electromagnetic induction heating coil are determined.
The heat affected zone of the material (fig. 5) gradually increased as the number of layers deposited on the component increased during the deposition process, and the heat affected zone sizes of the material were 0.834mm, 0.995mm, 1.609mm, 1.974mm, 2.302mm, respectively, as the number of layers gradually increased from one layer to five layers. The moving speed of the electromagnetic induction heating coil should satisfy the relation between the number of deposition layers in the above formula (10), and when C is less than or equal to 2, the moving speed v r of the electromagnetic induction heating coil satisfies: When C is more than or equal to 3 and less than or equal to 4, the moving speed v r of the electromagnetic induction heating coil meets the following conditions: When C is more than or equal to 5, the moving speed v r of the electromagnetic induction heating coil meets the following conditions:
When the component is subjected to in-situ self-heating effect heat treatment, the thickness of the reaction diffusion layer is related to electromagnetic induction heating time and heating temperature. The Gibbs free energy G of the component gradually increases along with the rise of the temperature; the relation between the diffusion distance and the diffusion activation energy of the atoms can be known by the Arrhenius equation in the formula (6), when the Gibbs free energy G exceeds the energy barrier (i.e. the diffusion activation energy) which is needed to be spanned by the atomic motion, the atoms of Ti and Al are separated from the constraint among the atoms, so that the atoms in the Ti and Al deposition layers react and diffuse mutually, and the purpose of expanding the phase region of the metal compound among TiAl is achieved. The thickness of the diffusion reaction layer and the diffusion time are parabolic:
x2＝k′1τk
In the above formula, x is the thickness of the diffusion layer; k is a material property correlation constant; d is a diffusion coefficient; τ k is the diffusion time; k' 1 is the diffusion layer growth coefficient; k is a constant; q is diffusion activation energy; r is a gas constant; t m is the temperature of the deposition body formed by the N deposition layers after being heated by the induction heating coil.
Because the TiAl intermetallic compound is wrapped by Ti and Al materials with excellent plasticity, the internal stress and the deformation of the TiAl intermetallic compound under the action of LDED forming cycle heat are absorbed by the Ti and Al materials, so that the internal stress and the deformation of the TiAl intermetallic compound are further inhibited from being absorbed by the Ti and Al materials, and further the formation of TiAl intermetallic compound cracks is inhibited. Subsequently, the in-situ thermal effect is utilized to drive the interlayer Ti and Al elements to diffuse and react to form TiAl intermetallic compounds, thereby forming a homogenized TiAl intermetallic compound member.
Claims (6)
1. An in-situ self-heating effect assisted 3D printing device for forming TiAl complex metal components comprises LDED forming equipment; the LDED forming equipment comprises a LDED control device, a printing platform and a laser printing deposition head, wherein the laser printing deposition head can deposit on the printing platform to form a deposition body according to a printing path preset in the LDED control device under the control of the LDED control device, and the deposition body comprises alternately laminated Ti deposition layers, al deposition layers and an interface layer between the Ti deposition layers and the Al deposition layers, and is characterized by further comprising arc induction heating equipment; the electric arc induction heating equipment comprises a lifting mechanism, an electric arc induction coil and an induction relay;
The arc induction coil is arranged outside the outline of the deposition body, is connected with a power supply after being connected with the induction relay in series, is connected with the power output end of the lifting mechanism, and can drive the arc induction coil to lift relative to the printing platform under the control of the LDED control device;
After each deposition layer of the deposition body deposits N deposition layers, synchronously carrying out induction heating on the part with the height H in the deposited N deposition layers by controlling a lifting mechanism; wherein:
；
Wherein: the total height of the N layers of deposition layers is represented, and N is more than or equal to 1; n represents a heat affected zone size parameter;
the arc induction coil is a spiral heating coil; the spiral heating coil comprises a plurality of layers of heating coils, and each layer of heating coil is provided with an induction relay;
Each heating coil corresponds to one deposition layer of the deposition body;
The LDED control device can dynamically turn on or off the corresponding induction relay on the spiral heating coil according to the deposition speed of each deposition layer in the deposition body;
the moving speed of the spiral heating coil The method meets the following conditions:
；
In the above-mentioned method, the step of, Indicating the number of layers of the deposited layer requiring induction heat treatment in the deposited body;，， respectively represent the speed proportional coefficients under different deposition layer number ranges, To the thickness of the deposited layer; The induction heating time required for a deposition body made up of N deposition layers is shown.
2. The apparatus for forming a TiAl complex metal component by in situ self-heating effect assisted 3D printing of claim 1 wherein the number of turns of heating coil required for a deposit of N layersThe method comprises the following steps:
；
Wherein: Representing ampere-turns per unit length of the heating coil, Representing the height of a part which needs to be subjected to induction heating in a deposition body formed by the N layers of deposition layers; Indicating the current of the heating coil.
3. The apparatus for forming a TiAl complex metal component by in-situ self-heating effect assisted 3D printing of claim 2 wherein the current of the heating coilThe method comprises the following steps:
；
Electric power of induction heating coil ：
；
Induction heat Q required for a deposition body made of N deposition layers:
；
Wherein: Representing the potential amplitude of the power supply; Representing an electric power factor; indicating thermal efficiency; Indicating the induction heating time required for a deposition body composed of N deposition layers; Representing the mass of a deposition body formed by N deposition layers; representing the specific heat capacity of the deposit; the temperature of a deposition body formed by N deposition layers after being heated by an induction heating coil is shown; Indicating the ambient temperature.
4. The device for forming a TiAl complex metal component by in-situ self-heating effect assisted 3D printing according to claim 3, wherein the temperature of a deposition body formed by N deposition layers after being heated by an induction heating coil is the same as the temperature of the deposition body formed by N deposition layers after being heated by the induction heating coilThe method meets the following conditions:
；
；
；
Wherein: Representing the height of a part which needs to be subjected to induction heating in a deposition body formed by the N layers of deposition layers; k is a material property correlation constant; d is a diffusion coefficient; Is diffusion time; Is the growth coefficient of the diffusion layer; k is a constant; is diffusion activation energy; r is a gas constant; t m is the temperature of the deposition body formed by the N deposition layers after being heated by the induction heating coil.
5. The apparatus for forming a TiAl complex metal member by in situ self-heating effect assisted 3D printing according to claim 1, wherein the LDED control means is controllable by modulating the laser power P, the laser scanning rate v 1 and the cooling rate v 2.
6. A method of in-situ self-heating effect assisted 3D printing of shaped TiAl complex metal components, realized on the basis of the apparatus of in-situ self-heating effect assisted 3D printing of shaped TiAl complex metal components according to claim 1, characterized in that it comprises the steps of:
Printing and forming a deposition body with preset thickness by adopting LDED forming process:
based on LDED forming equipment, adopting LDED forming technology, and alternately printing and forming Ti and Al metal powder according to a preset printing path to obtain a deposit body with preset thickness;
The deposition body comprises a laminated Ti deposition layer and an Al deposition layer, and an interface layer positioned at the interface joint of the Ti deposition layer and the Al deposition layer;
In the printing forming process of the deposition body, forming TiAl intermetallic compounds wrapped between the Ti deposition layer and the Al deposition layer in the interface layer by regulating and controlling the technological parameters of LDED forming technology so as to inhibit the formation of cracks of the TiAl intermetallic compounds;
step two, promoting the formation of TiAl intermetallic compounds in the interface layer of the deposit body by an in-situ heat post-treatment process:
Based on arc induction heating equipment, the deposition body obtained in the step one is subjected to induction heat treatment by adopting an in-situ heat post-treatment process so as to drive metal Ti atoms of the Ti deposition layer to diffuse towards the interface layer after being separated from the binding, and metal Al atoms of the Al deposition layer to diffuse towards the interface layer after being separated from the binding, thereby inducing the TiAl intermetallic compound formed in the interface layer to grow gradually so as to promote the formation of the TiAl intermetallic compound and lead the TiAl intermetallic compound between the Ti deposition layer and the Al deposition layer to be uniform.
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