CN117464022A - Additive manufacturing method of gamma-TiAl alloy - Google Patents

Additive manufacturing method of gamma-TiAl alloy Download PDF

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Publication number
CN117464022A
CN117464022A CN202311825893.9A CN202311825893A CN117464022A CN 117464022 A CN117464022 A CN 117464022A CN 202311825893 A CN202311825893 A CN 202311825893A CN 117464022 A CN117464022 A CN 117464022A
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gamma
powder
tial alloy
electron beam
thickness
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CN117464022B (en
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王一帆
贺卫卫
向长淑
李会霞
车倩颖
袁新波
张凯军
王元一
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Xi'an Sailong Additive Technology Co ltd
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Xi'an Sailong Additive Technology Co ltd
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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
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • 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
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • B22F1/142—Thermal or thermo-mechanical treatment
    • 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
    • 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
    • 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
    • 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
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Abstract

The application relates to an additive manufacturing method of gamma-TiAl alloy. Comprising the following steps: setting powder paving process parameters, wherein the powder paving process parameters comprise: the actual powder spreading thickness of each layer; obtaining effective penetration of an electron beam printing gamma-TiAl alloy sample in the test process, and obtaining a relation formula which needs to be met according to the theoretical cutting layer thickness and the actual powder spreading thickness; setting melting process parameters in selective melting, wherein the melting process parameters comprise energy density, and when the energy density is greater than the preset energy density, the effective penetration still can meet the relation; and carrying out electron beam selective melting forming on the gamma-TiAl alloy powder by using the powder laying process parameters and the melting process parameters. The method can regulate and control the cyclic heat treatment process of electron beams to the lower layer structure in the melting process, directly eliminate the lamellar gamma strip structure in the gamma-TiAl alloy, and greatly improve the strength of the alloy.

Description

Additive manufacturing method of gamma-TiAl alloy
Technical Field
The embodiment of the application relates to the technical field of additive manufacturing, in particular to an additive manufacturing method of gamma-TiAl alloy.
Background
The gamma-TiAl alloy has light weight, high specific strength, corrosion resistance, oxidation resistance and excellent room temperature and high temperature mechanical properties, and is a novel ideal material for aviation low pressure turbine blades. However, as a typical intermetallic compound material, the typical problems of low room temperature plasticity, poor high temperature deformability and the like exist, and the problems of high technical barrier, low yield and the like exist in the conventional process method for manufacturing the TiAl alloy blade. The powder bed electron beam selective melting technology has the advantages of near net forming, high preheating temperature (up to 1100 ℃), small residual stress, high production efficiency and the like, and becomes the first-choice rapid forming technology of the TiAl alloy complex structural member.
The powder bed electron beam selective melting technology is a powder spreading type 3D printing technology which takes electron beams as high-energy heat sources, wherein in the forming process, the electron beams firstly scan and preheat powder on a substrate, then selectively melt according to the section information of a part, then make a platform descend, repeat the powder spreading, preheating and melting processes, and finally form a three-dimensional solid part.
In the additive manufacturing process of the gamma-TiAl alloy, electron beams melt the powder of the current layer and repeatedly heat treat the solidified structure below the powder, and the repeated heat treatment process of the circulation often causes the coarse lamellar structure in the alloy to be transformed, so that the lamellar morphology of the circulation distribution of the fine two-state structure and the coarse equiaxial gamma-band structure is finally formed. As the grain size of the equiaxed gamma-band structure is coarser than that of the bi-state structure and the strength of the equiaxed gamma-band structure is insufficient, the strength of the alloy is lower than that of a sample in the forming direction (longitudinal direction), and the non-uniform structure is not beneficial to the industrialized application of TiAl alloy, especially the application in the aerospace field. Therefore, there is a need to effectively eliminate the gamma band structure to increase the strength of the alloy.
In the related art, in the method for regulating and controlling the structure in the selective melting process of TiAl alloy electron beam with the application number of CN202310168456.8, the brittle phase in the alloy is reduced, the plasticity of the alloy is improved, the good strength is maintained, the comprehensive improvement of the comprehensive performance of the alloy is realized, the forming defect of the obtained TiAl product is less, and the main structure is formed by typical equiaxed gamma phase and lamellar (alpha) 2 +γ) phase. The patent mainly achieves the aim of eliminating part of brittleness B by adding a preheating process before powder laying 2 The effect of the phases, however, the method does not eliminate the coarse equiaxed gamma band structure, and the structure of the obtained alloy is still the equiaxed gamma band structure and the fine two-state structure (gamma+alpha) 2 /gamma) alternately distributed mixed tissue. In a method for eliminating a layered structure of an electron beam 3D printing TiAl alloy, which is disclosed in the application number CN202310954846.8, the method mainly comprises the steps of heating the electron beam 3D printing TiAl alloy to 1200-1230 ℃, preserving heat for 1-3 hours, and then carrying out unidirectional forging to eliminate the layered heterogeneous uneven structure in an original ingot blank to obtain a uniform double-state or near-layer sheet structure. Although the method can eliminate lamellar structures (namely gamma band structures) in the TiAl alloy for electron beam 3D printing,but greatly increases the manufacturing cost of the alloy due to the addition of the forging process. In the high-strength TiAl alloy with the tensile strength of more than 750MPa and the additive manufacturing method thereof, the method adjusts the element component content of the alloy, increases the Nb content compared with the TiAl4822 alloy, adopts W to replace Mo, thereby ensuring that the alloy has better high-temperature strength and creep resistance. The method is mainly innovated from the viewpoint of alloy components and is not suitable for the industrialized production of TiAl alloy components with mature brands.
The technical means adopted in the related art cannot directly eliminate the coarse lamellar gamma band structure in the electron beam additive manufacturing process, and some lamellar structures need to be eliminated by an additional forging and pressing treatment, so that the manufacturing cost is greatly increased; some of the alloy components are adjusted to improve the alloy strength, which is not suitable for the industrial production of TiAl alloy components with mature marks.
Accordingly, there is a need to improve one or more problems in the related art as described above.
It is noted that this section is intended to provide a background or context for the technical solutions of the present application as set forth in the claims. The description herein is not admitted to be prior art by inclusion in this section.
Disclosure of Invention
It is an object of embodiments of the present application to provide a method of additive manufacturing of a gamma-TiAl alloy, which overcomes, at least to some extent, one or more of the problems due to limitations and disadvantages of the related art.
According to an embodiment of the application, a method for manufacturing an additive of a gamma-TiAl alloy comprises the following steps:
setting powder paving process parameters, wherein the powder paving process parameters comprise: the actual powder spreading thickness of each layer; the actual powder spreading thickness of each layer is calculated according to the theoretical slicing thickness, and in the process of an electron beam printing gamma-TiAl alloy test, the actual shrinkage thickness of each layer of gamma-TiAl alloy powder with the printing layer number being more than 5 is obtained by calculating, and the theoretical slicing thickness is obtained by slicing a three-dimensional model;
acquiring effective penetration of an electron beam printing gamma-TiAl alloy sample in the test process, and obtaining a relation of the effective penetration;
setting a melting process parameter in selective melting, wherein the melting process parameter comprises energy density, and when the energy density is larger than a preset energy density, the effective penetration still can meet the relation;
and carrying out electron beam selective melting forming on the gamma-TiAl alloy powder by utilizing the powder spreading technological parameters and the melting technological parameters.
In an embodiment of the present application, the performing electron beam selective melt forming on the γ -TiAl alloy powder by using the powder laying process parameter and the melting process parameter includes:
preheating a substrate in a forming chamber;
paving the gamma-TiAl alloy powder on the preheated substrate according to the powder paving process parameters so as to perform powder paving;
carrying out powder preheating on the gamma-TiAl alloy powder on the substrate;
carrying out zone-selection melting on the preheated gamma-TiAl alloy powder according to the melting technological parameters;
performing thermal compensation on the powder bed after the selected area is melted;
repeating the steps of powder paving, powder preheating, selective melting and thermal compensation until the target gamma-TiAl alloy is obtained.
In an embodiment of the present application, a calculation formula of the actual powder spreading thickness of each layer is:
H=an+h（1）
wherein H represents the actual powder spreading thickness of each layer, H represents the theoretical slicing thickness, and an represents the actual shrinkage thickness of each layer of gamma-TiAl alloy powder after the number of printing layers is more than 5 in the test process of printing gamma-TiAl alloy by an electron beam.
In an embodiment of the present application, in an electron beam printing γ -TiAl alloy test process, a calculation formula of the actual shrinkage thickness of each γ -TiAl alloy powder after the number of printing layers is greater than 5 is:
an=h（1-k）/k（2）
wherein k represents the ratio of the bulk density of the gamma-TiAl alloy powder to the bulk density of the gamma-TiAl alloy.
In an embodiment of the present application, the effective penetration is expressed as follows:
m≥H+2h（3）
wherein m represents the effective penetration of the electron beam printed gamma-TiAl alloy sample during the test.
In an embodiment of the present application, the energy density is calculated according to a scan voltage, a scan current, a scan speed, a scan pitch and the theoretical slice thickness during electron beam scanning, and a calculation formula of the energy density is:
ρ body =UI/vdh（4）
Wherein ρ is Body The energy density, U, the scanning voltage, I, the scanning current, v, the scanning speed and d the scanning interval are expressed.
In one embodiment of the present application, the preset energy density is 45J/mm 3 。
In an embodiment of the present application, the theoretical slicing thickness ranges from 30 μm to 100 μm.
In an embodiment of the present application, the preheating the substrate in the forming chamber includes:
and pre-placing the gamma-TiAl alloy powder in a powder bin.
In one embodiment of the present application, the pre-placing the γ -TiAl alloy powder in the powder bin, then comprises:
and vacuumizing the forming chamber and the gun chamber respectively, and filling inert gas so that the vacuum degree of the forming chamber is larger than the first preset vacuum degree, and the vacuum degree of the gun chamber reaches the second preset vacuum degree.
The technical scheme provided by the embodiment of the application can comprise the following beneficial effects:
according to the embodiment of the application, through the method, the layered gamma strip structure in the gamma-TiAl alloy is directly eliminated by regulating and controlling the powder spreading process parameters, the effective penetration and the melting process parameters and carrying out electron beam selective melting forming on the gamma-TiAl alloy powder according to the powder spreading process parameters and the melting process parameters so as to regulate and control the cyclic heat treatment process of electron beams to the lower layer structure in the melting process, and the strength of the alloy is greatly improved.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the application and together with the description, serve to explain the principles of the application. It is apparent that the drawings in the following description are only some embodiments of the present application, and that other drawings may be obtained from these drawings without inventive effort for a person of ordinary skill in the art.
FIG. 1 illustrates a flow chart of steps of a method of additive manufacturing of a gamma-TiAl alloy in an exemplary embodiment of the present application;
FIG. 2 shows a schematic representation of the variation in powder layer thickness during printing in an exemplary embodiment of the present application;
FIG. 3 shows a schematic view of formation temperature intervals of equiaxed gamma banding and bimodal organization in an electron beam printed gamma TiAl alloy in an exemplary embodiment of the present application;
FIG. 4 illustrates a schematic view of effective penetration measurement of an electron beam printed gamma-TiAl alloy coupon in an exemplary embodiment of the present application;
FIG. 5 shows a metallographic structure diagram of a Ti-48Al-2Cr-2Nb alloy sample prepared in an exemplary embodiment of the present application;
FIG. 6 is a diagram showing a metallographic structure of a Ti-48Al-2Cr-2Nb alloy sample when electron beam penetration is insufficient in an exemplary embodiment of the present application;
FIG. 7 shows a metallographic structure diagram of a Ti-48Al-2Cr-2Nb alloy sample at the time of insufficient energy density in the exemplary embodiment of the present application.
Detailed Description
Example embodiments will now be described more fully with reference to the accompanying drawings. However, the exemplary embodiments may be embodied in many forms and should not be construed as limited to the examples set forth herein; rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the concept of the example embodiments to those skilled in the art. The described features, structures, or characteristics may be combined in any suitable manner in one or more embodiments.
Furthermore, the drawings are only schematic illustrations of embodiments of the present application and are not necessarily drawn to scale.
The additive manufacturing of the gamma-TiAl alloy generally adopts a powder bed electron beam selective melting process, but the microstructure of the gamma-TiAl alloy formed by powder bed electron beam selective melting generally presents a coarse equiaxed gamma strip structure and a fine binary structure (gamma+alpha) along the forming direction 2 /gamma) alternately distributed mixed tissue. Wherein, the coarse equiaxed gamma band structure is unfavorable for improving the strength of the alloy, and the excessive equiaxed gamma bands can cause the decrease of the strength of the alloy. Therefore, effective elimination of the gamma band structure is critical to improving the strength of the alloy. Accordingly, an additive manufacturing method of a gamma-TiAl alloy is provided in the present example embodiment. Referring to what is shown in fig. 1, the method may include: step S101 to step S104.
Wherein, step S101: setting powder paving process parameters, wherein the powder paving process parameters comprise: the actual powder spreading thickness of each layer; the actual powder spreading thickness of each layer is calculated according to the theoretical slicing thickness, and in the process of an electron beam printing gamma-TiAl alloy test, the actual shrinkage thickness of each layer of gamma-TiAl alloy powder after the number of printing layers is more than 5 is calculated, and the theoretical slicing thickness is obtained by slicing a three-dimensional model.
Step S102: and obtaining effective penetration of the electron beam printing gamma-TiAl alloy sample in the test process, and obtaining a relation of the effective penetration.
Step S103: and setting melting process parameters in selective melting, wherein the melting process parameters comprise energy density, and when the energy density is greater than the preset energy density, the effective penetration still can meet the relation.
Step S104: and carrying out electron beam selective melting forming on the gamma-TiAl alloy powder by using the powder laying process parameters and the melting process parameters.
It can be appreciated that in the electron beam selective melt forming process of the γ -TiAl alloy powder, in order to eliminate lamellar γ -band structure in the γ -TiAl alloy, the strength of the γ -TiAl alloy is improved. The method needs to set powder spreading technological parameters and obtain the effective penetration and the relation to be satisfied by the effective penetration of the electron beam printing gamma-TiAl alloy sample in the test process. In addition, it is also necessary to set the melting process parameters at the time of selective melting. And then carrying out electron beam selective melting forming on the gamma-TiAl alloy powder based on the powder laying process parameters and the melting process parameters.
Ti is an element symbol of Titanium, and Ti is a metal chemical element. Al is an element symbol of aluminum, and Al is a metal chemical element, and is called aluminum.
Next, respective portions of the above-described additive manufacturing method of a γ -TiAl alloy in the present exemplary embodiment will be described in more detail with reference to fig. 2 to 7.
In step S101, the present application needs to calculate the powder spreading process parameters including the actual powder spreading thickness of each layer before setting the powder spreading process parameters. And when calculating the actual powder spreading thickness of each layer, calculating according to the theoretical cutting thickness and the actual shrinkage thickness of each layer of gamma-TiAl alloy powder after the printing layer number is more than 5 in the electron beam printing gamma-TiAl alloy test process. The theoretical slicing thickness can be obtained by slicing a three-dimensional model of the gamma-TiAl alloy in slicing software.
Calculation of the actual shrink thickness: since the powder solidifies into a dense solid structure after being melted by the electron beam, shrinkage of the powder layer occurs due to a significant density difference between the powder and the dense solid structure. In the process of electron beam printing gamma-TiAl alloy test, the actual shrinkage thickness of gamma-TiAl alloy powder of each layer gradually tends to a stable value when the printing layer number n is continuously increased, namely when the printing layer number n is larger than 5, so that the actual shrinkage thickness of the stable value is formed, namely in the process of electron beam printing gamma-TiAl alloy test, the actual shrinkage thickness of gamma-TiAl alloy powder of each layer after the printing layer number n is larger than 5.
Thus, as shown in FIG. 2, the actual powder thickness H of each layer is calculated from the actual shrinkage thickness an and the theoretical cut thickness H, which form stable values. Namely, the calculation formula of the actual powder paving thickness of each layer is as follows:
H=an+h（1）
in the test process of the gamma-TiAl alloy printed by the electron beam, the calculation formula of the actual shrinkage thickness of each gamma-TiAl alloy powder after the number of printing layers is more than 5 is as follows:
an=h（1-k）/k（2）
wherein k represents the ratio of the bulk density of the gamma-TiAl alloy powder to the bulk density of the gamma-TiAl alloy.
In step S102, the effective penetration of the electron beam printed gamma-TiAl alloy sample during the measurement test is m. In the electron beam printing gamma-TiAl alloy test process, the electron beam printing gamma-TiAl alloy sample has the uppermost layer structure, and the uppermost layer has the original shape of the full-layer sheet or near-layer sheet structure maintained as no subsequent cyclic heat treatment process is carried out on the uppermost layer structure. The application defines that the distance from the top end of the whole layer or near layer tissue at the upper part of the gamma-TiAl alloy sample to the fine grain region is the effective penetration of an electron beam molten pool, and the effective penetration of the electron beam molten pool is the effective penetration of the gamma-TiAl alloy sample printed by an electron beam in the test process. The effective penetration m of the electron beam printing gamma-TiAl alloy sample in the test process can be measured by a metallographic method. When the effective penetration is measured by using a metallographic method, the effective penetration is measured for 3 times at different positions of the same gamma-TiAl alloy sample, and the average value is taken as the effective penetration. Metallographic techniques may be understood with reference to the prior art, which is not limiting in this application.
In step S103, during the formation of the γ -TiAl alloy, the electron beam performs cyclic heat treatment on one or more layers of solidified structures below, and when the electron beam is able to penetrate the 2 layers of structures below the surface powder, the cyclic heat treatment effect is ensured to be good, and the bonding state between the layers is optimal. The effective penetration of the electron beam molten pool can be regulated by the position of an electron beam focusing plane and the current, and the theoretical slicing thickness h can be set by slicing software of a three-dimensional model. The actual powder paving thickness, the theoretical cutting thickness h and the effective penetration m of each layer are adjusted, so that the effective penetration m meets the following relation:
m≥H+2h（3）
when the effective penetration m satisfies the above relation, good forming quality can be ensured.
In step S104, a melting process parameter including an energy density at the time of selective melting is set. The application is when setting up the energy density, needs to set up the energy density and be greater than the energy density of predetermineeing. This is because: when the electron beam carries out cyclic heat treatment on the structure below the powder layer, the coarse lamellar structure in the gamma-TiAl alloy can be degenerated, and finally a fine bi-state structure (gamma+alpha) is formed 2 And/gamma) and equiaxed gamma band tissue cycle. Wherein the coarse equiaxed gamma bands are detrimental to the improvement of the strength of the TiAl alloy (especially in Z-direction samples), the amount of equiaxed gamma bands being related to the actual heat input during printing. The magnitude of the heat input is in turn related to the magnitude of the energy density, the greater the heat input. The larger the heat input is, the larger the volume of the molten pool is, the effective penetration can be achieved, and the heat treatment effect on the lower layer tissue is stronger. When the energy density is larger than the preset energy density, the effective penetration still can meet the relation, and further, the preset energy density is 45J/mm 3 . According to the TiAl alloy phase diagram, the heat treatment temperature for forming the gamma band structure is about 1050-1125 ℃ and the heat treatment temperature for forming the binary structure is about 1250 ℃, the details are shown in figure 3, L represents liquidus, and the TiAl alloy phase diagram contains alpha phase, beta phase and alpha phase 2 +γ) phase and (α+γ) phase.
Energy density ρ when electron beam is input Body Higher than 45J/mm 3 When the electron beam is used for circularly heat-treating the tissue below the powder layer, the temperature of the biphasic region is 1250 ℃ so that the original equiaxial gamma band is converted into a fine two-state tissue (gamma+alpha) 2 Gamma) so as to achieve the effects of eliminating gamma band tissues and improving alloy strength.
The energy density is calculated as:
ρ body =UI/vdh（4）
Wherein U is the scanning voltage, I is the scanning current, v is the scanning speed, d is the scanning interval, and h is the theoretical slice thickness. By adjusting various technological parameters, ρ is formed Body ＞45J/mm 3 Thereby ensuring the elimination of gamma strips and improving the strength of the alloy.
In the embodiment of the application, the electron beam selective melting forming is carried out on the gamma-TiAl alloy powder according to the powder laying technological parameters, the effective penetration and the melting technological parameters, so that the cyclic heat treatment process of electron beams in the melting process on the lower layer tissues is regulated and controlled, the layered gamma strip tissues in the gamma-TiAl alloy are directly eliminated, and the strength of the alloy is greatly improved.
In one embodiment, electron beam selective melt forming of gamma-TiAl alloy powder using the powder laying process parameters and melting process parameters described above includes:
preheating a substrate in a forming chamber;
paving gamma-TiAl alloy powder on the preheated substrate according to the powder paving process parameters so as to perform powder paving;
carrying out powder preheating on gamma-TiAl alloy powder on a substrate;
carrying out zone-selection melting on the preheated gamma-TiAl alloy powder according to melting technological parameters;
performing thermal compensation on the powder bed after the selected area is melted;
repeating the steps of powder paving, powder preheating, selective melting and thermal compensation until the target gamma-TiAl alloy is obtained.
It will be appreciated that in the three-dimensional forming process, first, when the substrate of the forming chamber is preheated by the electron beam, the substrate needs to be preheated to a first preset temperature. Secondly, after the substrate is preheated, the gamma-TiAl alloy powder needs to be paved on the preheated substrate according to the set powder paving process parameters, namely according to the actual powder paving thickness of each layer. And preheating the gamma-TiAl alloy powder paved on the preheated substrate to a second preset temperature by utilizing an electron beam. In addition, according to the melting process parameters, namely according to the energy density, the preheated gamma-TiAl alloy powder is subjected to selective melting, wherein the energy density is larger than the preset energy density. And then carrying out thermal compensation on the powder bed after the selective melting. The magnitude of the first preset temperature and the magnitude of the first preset temperature can be set according to practical situations, which is not limited in the application.
And finally, repeating the steps of powder paving, powder preheating, zone selection melting and thermal compensation until all layers are processed to obtain the target gamma-TiAl alloy.
The preheating of the substrate in the forming chamber includes:
the gamma-TiAl alloy powder is placed in a powder bin in advance.
And vacuumizing the forming chamber and the gun chamber respectively, and filling inert gas so that the vacuum degree of the forming chamber is larger than the first preset vacuum degree, and the vacuum degree of the gun chamber reaches the second preset vacuum degree.
It should be noted that the purpose of preheating the substrate and preheating the powder is to prevent the powder blowing phenomenon. The purpose of thermal compensation of the powder bed is to prevent the powder blowing phenomenon caused by low temperature of the powder bed on one hand, and to reduce thermal stress and prevent cracking of the target gamma-TiAl alloy on the other hand.
In one embodiment, the actual powder thickness of each layer is calculated as:
H=an+h（1）
wherein H represents the actual powder spreading thickness of each layer, H represents the theoretical slicing thickness, and an represents the actual shrinkage thickness of each layer of gamma-TiAl alloy powder after the number of printing layers is more than 5 in the test process of printing gamma-TiAl alloy by an electron beam.
It will be appreciated that the actual powder thickness of each layer can be calculated according to equation (1) above.
In one embodiment, in the process of the electron beam printing gamma-TiAl alloy test, the calculation formula of the actual shrinkage thickness of each gamma-TiAl alloy powder after the number of printing layers is more than 5 is as follows:
an=h（1-k）/k（2）
where k represents the ratio of the bulk density of the powder to the bulk density of the gamma-TiAl alloy.
It will be appreciated that in the process of the electron beam printing gamma-TiAl alloy test, the actual shrinkage thickness of each gamma-TiAl alloy powder layer with the number of printing layers being greater than 5 can be calculated according to the above formula (2).
In one embodiment, the effective penetration is related by:
m≥H+2h（3）
wherein m represents the effective penetration of the gamma-TiAl alloy sample in the process of the gamma-TiAl alloy test by electron beam printing.
It can be appreciated that the effective penetration of the gamma-TiAl alloy sample in the process of the electron beam printing gamma-TiAl alloy test meets the above relation (3), thereby ensuring good forming quality.
In one embodiment, the energy density is calculated according to the scan voltage, the scan current, the scan speed, the scan pitch and the theoretical slice thickness during the electron beam scan, and the energy density is calculated according to the following formula:
ρ body =UI/vdh（4）
Wherein ρ is Body The energy density, U, the scanning voltage, I, the scanning current, v, the scanning speed and d the scanning interval are expressed.
It will be appreciated that the energy density can be calculated according to equation (4) above.
In one embodiment, the preset energy density is 45J/mm 3 。
It will be appreciated that the predetermined energy density is 45J/mm 3 When the energy density is greater than 45J/mm 3 When the alloy is melted in the selected area, the gamma band can be eliminated, and the strength of the alloy is improved.
In one embodiment, the theoretical slice thickness ranges from 30 to 100 μm.
In one embodiment, preheating the substrate within the forming chamber, previously comprises:
the gamma-TiAl alloy powder is placed in a powder bin in advance.
In one embodiment, the gamma-TiAl alloy powder is pre-placed within the powder bin, followed by:
and vacuumizing the forming chamber and the gun chamber respectively, and filling inert gas so that the vacuum degree of the forming chamber is larger than the first preset vacuum degree, and the vacuum degree of the gun chamber reaches the second preset vacuum degree.
The present application is further illustrated by example 1 below.
Example 1:
the gamma-TiAl alloy printed in this example is Ti-48Al-2Cr-2Nb alloy, the gamma-TiAl alloy powder used is spherical Ti-48Al-2Cr-2Nb alloy powder prepared by a plasma rotary electrode method, the grain size interval of the spherical Ti-48Al-2Cr-2Nb alloy powder is 45-150 mu m, and the apparent density ρ of the spherical Ti-48Al-2Cr-2Nb alloy powder is higher than that of the spherical Ti-48Al-2Cr-2Nb alloy powder Loose dress 2.35g/cm 3 The entity density rho of Ti-48Al-2Cr-2Nb alloy Entity 4g/cm 3 ，k=ρ Loose dress /ρ Entity =0.5875. Before printing, the amount of melting defocus is adjusted to 0V so that the condensing plane of the electron beam and the substrate surface are on the same level.
Step one: the actual powder thickness H of each layer was calculated. The theoretical slice thickness H is set to be 50 μm by slice software of the three-dimensional model, the actual shrinkage thickness is obtained to be 35.1 μm according to an=h (1-k)/k, and the actual powder laying thickness H is obtained to be 85.1 μm according to H=an+h.
Step two: (1) And measuring the effective penetration d of the electron beam printing gamma-TiAl alloy sample in the test process. FIG. 4 shows the microstructure of the powder bed electron beam selected zone at the top end of the molten gamma-TiAl alloy sample, showing obvious lamellar morphology. The distances from the top of the lamellar structure to the fine grain region were measured at different positions and were 192.6 μm, 206.2 μm and 211.3 μm, respectively, and the effective penetration m of the electron beam printed γ -TiAl alloy was found to be 203.4 μm by averaging.
(2) And H, H and m are regulated so that m is more than or equal to H+2h. By comparison, the effective penetration depth m=203.4 μm > h+2h=185.1 μm of the γ -TiAl alloy printed by electron beam in this example satisfies the requirements.
Step three: adjusting the heat input so that the energy density ρ Body ＞45J/mm 3 . In this embodiment, the scanning voltage is u=60 kV, the scanning current is i=13.5 mA, the scanning speed is v=3.5 m/s, the scanning pitch d=0.1 mm, and the theoretical slice thickness h=50 μm, and the energy density ρ is calculated Body =46.3J/mm 3 Meeting the requirements.
Step four: and (5) melting and forming the powder bed in a selected area by using electron beams. The specific process is as follows: (1) in the powder bed electron beamPre-placing Ti-48Al-2Cr-2Nb alloy powder with the diameter of 45-150 mu m in a powder bin in a selective melting device; (2) vacuumizing the forming chamber and the gun chamber and filling inert gas which is helium gas, so that the vacuum degree of the forming chamber reaches 1.4-2 multiplied by 10 -1 Pa, the vacuum degree of the gun chamber reaches 1.8-2.5X10 -4 Pa; (3) heating the substrate to 1100 ℃ by using an electron beam; (4) powder is paved on the substrate by utilizing a powder taking device according to the powder paving process parameters; (5) preheating Ti-48Al-2Cr-2Nb alloy powder on the substrate by utilizing an electron beam, wherein the preheating current is 48mA, and the preheating time is 27s; (6) carrying out zone-selection melting on the preheated Ti-48Al-2Cr-2Nb alloy powder according to melting technological parameters; (7) carrying out thermal compensation on the powder bed after the selected area is melted, wherein the thermal compensation current is 48mA, and the thermal compensation time is 17s; (8) the powder bed descending process of powder paving, powder preheating, selective melting, thermal compensation and powder bed descending is repeated until all layers are processed.
Cr is an element symbol of Chromium, which is called chrome in its entirety, and Chromium is a metal element. Nb is an element symbol of Niobium, which is known as Niobium throughout english, and Niobium is a metal element.
The metallographic structure of the Ti-48Al-2Cr-2Nb alloy sample prepared in the embodiment is shown in fig. 4, the equiaxial gamma band structure is basically eliminated in the diagram, the mechanical property is shown in the process 1 in the table 1, and the average tensile strength reaches 763.68MPa.
When the effective penetration of the electron beam is 120-160 mu m and m is not more than H+2h (the thickness of a theoretical slicing layer is 50 mu m), the metallographic structure of the formed Ti-48Al-2Cr-2Nb alloy is shown as a figure 5, the volume ratio of an equiaxed gamma strip structure in the figure is more than half, and the fine grain area of a binary structure is obviously reduced. The mechanical properties are shown in Table 1 as process 2, and the average tensile strength is reduced to 605.67MPa.
When the effective penetration of the electron beam is 185.1 μm as in the example, m is more than or equal to H+2h, but the energy density is 32.4J/mm 3 In the process, the metallographic structure of the prepared Ti-48Al-2Cr-2Nb alloy is shown in fig. 6, and the coarse equiaxial gamma band structure and the binary structure fine grain are alternately distributed in the graph, and the mechanical property is shown in the process 3 in the table 1, and the average tensile strength is 672.36MPa.
The metallographic structure of the Ti-48Al-2Cr-2Nb alloy sample with insufficient energy density is shown in FIG. 7.
As can be seen from the comparison, the mechanical property of the Ti-48Al-2Cr-2Nb alloy prepared by the method can stably reach more than 750MPa in the Z direction, and is far higher than the level of a conventional powder bed electron beam selective melting Ti-48Al-2Cr-2Nb alloy sample.
TABLE 1 tensile Strength of samples of Ti-48Al-2Cr-2Nb alloy in Z direction under different technologies
In the description of this specification, the terms "first," "second," and the like are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implicitly indicating the number of technical features indicated. Thus, a feature defining "a first" or "a second" may explicitly or implicitly include one or more such feature.
In the description of the present specification, a description referring to the terms "one embodiment," "some embodiments," "examples," "particular examples," or "some examples," etc., means that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the present application. In this specification, schematic representations of the above terms are not necessarily directed to the same embodiment or example. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples. Furthermore, one skilled in the art can combine and combine the different embodiments or examples described in this specification.
Other embodiments of the present application will be apparent to those skilled in the art from consideration of the specification and practice of the invention disclosed herein. This application is intended to cover any variations, uses, or adaptations of the application following, in general, the principles of the application and including such departures from the present disclosure as come within known or customary practice within the art to which the application pertains.

Claims (10)

1. A method of additive manufacturing of a gamma-TiAl alloy, the method comprising:
setting powder paving process parameters, wherein the powder paving process parameters comprise: the actual powder spreading thickness of each layer; the actual powder spreading thickness of each layer is calculated according to the theoretical slicing thickness, and in the process of an electron beam printing gamma-TiAl alloy test, the actual shrinkage thickness of each layer of gamma-TiAl alloy powder with the printing layer number being more than 5 is obtained by calculating, and the theoretical slicing thickness is obtained by slicing a three-dimensional model;
acquiring effective penetration of an electron beam printing gamma-TiAl alloy sample in the test process, and obtaining a relation of the effective penetration;
setting a melting process parameter in selective melting, wherein the melting process parameter comprises energy density, and when the energy density is larger than a preset energy density, the effective penetration still can meet the relation;
and carrying out electron beam selective melting forming on the gamma-TiAl alloy powder by utilizing the powder spreading technological parameters and the melting technological parameters.
2. The method of additive manufacturing of a γ -TiAl alloy according to claim 1, wherein said electron beam selective melt forming of the γ -TiAl alloy powder using the powder laying process parameters and the melting process parameters comprises:
preheating a substrate in a forming chamber;
paving the gamma-TiAl alloy powder on the preheated substrate according to the powder paving process parameters so as to perform powder paving;
carrying out powder preheating on the gamma-TiAl alloy powder on the substrate;
carrying out zone-selection melting on the preheated gamma-TiAl alloy powder according to the melting technological parameters;
performing thermal compensation on the powder bed after the selected area is melted;
repeating the steps of powder paving, powder preheating, selective melting and thermal compensation until the target gamma-TiAl alloy is obtained.
3. The additive manufacturing method of a gamma-TiAl alloy according to claim 1, wherein the actual powder thickness of each layer is calculated by the formula:
H=an+h（1）
wherein H represents the actual powder spreading thickness of each layer, H represents the theoretical slicing thickness, and an represents the actual shrinkage thickness of each layer of gamma-TiAl alloy powder after the number of printing layers is more than 5 in the test process of printing gamma-TiAl alloy by an electron beam.
4. A method of additive manufacturing of a γ -TiAl alloy according to claim 3, wherein in an electron beam printing test of a γ -TiAl alloy, the actual shrinkage thickness of each layer of the γ -TiAl alloy powder after the number of printing layers is greater than 5 is calculated as:
an=h（1-k）/k（2）
wherein k represents the ratio of the bulk density of the gamma-TiAl alloy powder to the bulk density of the gamma-TiAl alloy.
5. A method of additive manufacturing of a γ -TiAl alloy according to claim 3, wherein the effective penetration is expressed by the relationship:
m≥H+2h（3）
wherein m represents the effective penetration of the electron beam printed gamma-TiAl alloy sample during the test.
6. The method for manufacturing an additive for a γ -TiAl alloy according to claim 3, wherein the energy density is calculated from a scanning voltage, a scanning current, a scanning speed, a scanning pitch, and the theoretical slice thickness at the time of electron beam scanning, and the energy density is calculated by the following formula:
ρ body =UI/vdh（4）
Wherein ρ is Body The energy density, U, the scanning voltage, I, the scanning current, v, the scanning speed and d the scanning interval are expressed.
7. The method of additive manufacturing of gamma-TiAl alloy according to claim 1, wherein the preset energy density is 45J/mm 3 。
8. The additive manufacturing method of gamma-TiAl alloy according to claim 1, wherein the theoretical slicing thickness is in a range of 30-100 μm.
9. The method of additive manufacturing of γ -TiAl alloy according to claim 2, wherein the preheating of the substrate in the forming chamber, previously comprises:
and pre-placing the gamma-TiAl alloy powder in a powder bin.
10. The method of additive manufacturing of a gamma-TiAl alloy according to claim 9, wherein the pre-placing of the gamma-TiAl alloy powder in a powder bin, after which comprises:
and vacuumizing the forming chamber and the gun chamber respectively, and filling inert gas so that the vacuum degree of the forming chamber is larger than the first preset vacuum degree, and the vacuum degree of the gun chamber reaches the second preset vacuum degree.
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