CN111922336A - Method for reducing texture strength of laser three-dimensional forming high-temperature alloy and application - Google Patents
Method for reducing texture strength of laser three-dimensional forming high-temperature alloy and application Download PDFInfo
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- 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
- 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
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Abstract
The invention relates to a method for reducing texture strength of laser three-dimensional forming high-temperature alloy and application thereof. Selecting a laser with laser energy conforming to Gaussian distribution; carrying out layer-by-layer melting deposition on the alloy powder flow conveyed by the carrier gas on a metal substrate; the laser scanning adopts a method of interlamination staggered scanning, and the moving directions of laser melting baths in adjacent deposition layers are different. The material of the alloy substrate is Inconel 718 alloy. The diameter of the laser beam is more than or equal to 5 mm. The power of the laser is more than or equal to 4 kW. The powder feeding speed is more than or equal to 30 g/min. The texture strength MUD of the large-scale complex nickel-based high-temperature alloy component formed by the laser three-dimensional forming is 3.37, and the texture strength MUD close to that of a forged piece is 1.00.
Description
Technical Field
The invention belongs to the technical field of laser additive manufacturing, and particularly relates to a method for reducing texture intensity of laser three-dimensional forming high-temperature alloy and application thereof.
Background
The information in this background section is only for enhancement of understanding of the general background of the invention and is not necessarily to be construed as an admission or any form of suggestion that this information forms the prior art that is already known to a person of ordinary skill in the art.
The laser three-dimensional forming technology can realize high-performance, fully-compact, integrated, mold-free and near-net forming of three-dimensional complex metal components, and is proved to be an economical and effective forming method for difficult-to-process materials such as nickel-based high-temperature alloy and the like. At present, the laser stereolithography technology is widely applied in the industries of aviation, aerospace, navigation, nuclear power, petroleum and the like.
However, during the laser three-dimensional forming process, the solid/liquid interface of the laser molten pool has higher temperature gradient (more than or equal to 10)5K/m), inducing the effect of epitaxial growth of the internal tissue. Generally speaking, the internal organization structure of the laser three-dimensional forming nickel-based superalloy component is represented by epitaxially grown columnar crystals, namely, the columnar crystals have a strong crystallographic texture, which inevitably causes anisotropy of mechanical properties and increases the tendency of fracture along the crystals in the deformation process. Therefore, changing the columnar crystal morphology in the laser three-dimensional forming nickel-based superalloy and reducing the texture strength are important ways for improving the mechanical property and changing the anisotropy.
At present, three methods for reducing texture strength of a laser three-dimensional forming nickel-based superalloy component are mainly used: (1) a remelting depth reducing method, (2) a solution heat treatment method, and (3) an ultrasonic vibration applying method. (1) During the laser stereoforming process, columnar crystal-isometric crystal transformation can occur at the top of the molten pool due to the reduction of temperature gradient, so that a layer of very thin isometric crystal area (the thickness is less than or equal to 500 mu m) exists at the top of the deposition layer. The method of reducing the remelting depth to reduce the texture strength is to reduce the remelting depth so that the equiaxed crystal layer is not completely melted but partially retained when the next layer is deposited. The reserved equiaxed crystal layer cuts off the epitaxial growth of columnar crystal to form a bamboo joint-shaped structure, thereby reducing the texture strength. However, the process method is complicated and has certain difficulty in realization due to the fact that the equiaxed crystal layer is thin and the remelting depth is difficult to control; in addition, the "bamboo" structure still has strong orientation, so the effectiveness of the method for reducing the texture strength is limited. (2) When the temperature of the solution heat treatment reaches the recrystallization temperature (generally 1100 ℃), the sedimentary structure is recrystallized to generate a new crystal boundary, and the columnar crystal is equiaxial to a certain degree, so that the texture strength is reduced. However, researches show that the columnar crystals are difficult to completely eliminate by the solution heat treatment, and the performance of the columnar crystals still has anisotropy; moreover, for large nickel-based high-temperature alloy components, the solution heat treatment system puts high requirements on heat treatment equipment and a heat treatment process. Therefore, the method for reducing the texture strength by the solution heat treatment has the characteristics of higher cost, long production period, complex process and the like. (3) In the process of laser three-dimensional forming, although the existence time of a laser molten pool at a certain position is short (0.1-1s), by utilizing the cavitation effect (more than or equal to 20000 times/s) of ultrasonic vibration, equiaxial crystal nucleation and growth can be induced, the transformation of columnar crystal orientation equiaxial crystal is realized, and the texture intensity is effectively reduced. However, as the deposition height and the shape of the deposition layer are changed, the ultrasonic vibration frequency is changed, so that the stability of the ultrasonic vibration is influenced; in addition, the height of the deposition layer is in the half-wavelength range of the ultrasonic wave, the amplitude of the ultrasonic vibration can be changed from zero to the maximum value along the direction of the deposition height, and the position of the zero amplitude can influence the effective application of the ultrasonic vibration; it is noted that for large complex components, ultrasonic vibrations cannot be applied effectively at all.
The inventor finds that the existing methods for reducing the texture strength of the laser three-dimensional forming member are difficult to realize the reduction of the texture strength with simple process, low cost and high reliability, and particularly the reduction of the texture strength of a large-scale complex member faces a greater challenge.
Disclosure of Invention
In view of the above problems in the prior art, the present invention is directed to a method and application for reducing the texture strength of laser stereolithography superalloy. The invention provides a laser three-dimensional forming method, which is used for treating nickel-based high-temperature alloy, particularly large complex components to obtain components with low texture strength and controlling the texture strength at any position.
In order to solve the technical problems, the technical scheme of the invention is as follows:
in a first aspect, a method for reducing the texture strength of a laser stereolithography superalloy, the method comprising:
selecting a laser with laser energy conforming to Gaussian distribution;
carrying out layer-by-layer melting deposition on the alloy powder flow conveyed by the carrier gas on a metal substrate;
the laser scanning adopts a method of interlamination staggered scanning, and the moving directions of laser melting baths in adjacent deposition layers are different.
Selecting a laser with laser energy conforming to Gaussian distribution and large laser beam diameter to realize that the arc of a fusion line at the bottom of a laser melting pool has large curvature; the change of the moving direction of the laser molten pool in the adjacent deposition layer directly changes the direction of the temperature gradient, and when the change of the direction of the temperature gradient exceeds 45 degrees, the growing direction of the dendrite is changed, such as the dendrite is turned from the <001> direction to the <010> direction or the <100> direction, namely the formation of the turning dendrite is promoted.
The texture strength close to that of a forging is realized.
The ultrasonic vibration method cannot achieve uniformity of a large member. The traditional laser three-dimensional forming method can cause the texture strength to deviate from that of a forged piece greatly.
In a second aspect, the method for reducing the texture strength of the laser stereolithography superalloy is applied to the field of laser stereolithography of superalloys.
One or more technical schemes of the invention have the following beneficial effects:
by changing the technological parameters of the laser three-dimensional forming process, the method effectively reduces the texture strength of the laser three-dimensional forming nickel-based superalloy large-scale complex component, and has the following remarkable advantages:
(1) based on the characteristics of point-by-point deposition and layer-by-layer accumulation of the laser stereolithography technology, the texture intensity at any position of a deposition layer can be effectively regulated and controlled, and the method is simple and convenient to operate, low in cost and high in reliability;
(2) the texture strength (MUD ═ 3.37) of the large-scale complex nickel-base superalloy component formed by the laser three-dimensional forming can be close to that of a forged piece (MUD ═ 1.00).
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, are included to provide a further understanding of the invention, and are incorporated in and constitute a part of this specification, illustrate embodiments of the invention and together with the description, serve to explain the invention and not to limit the invention.
Fig. 1 is a technical route diagram for reducing texture intensity of a large-scale complicated laser stereolithography Inconel 718 alloy component;
FIG. 2 is a schematic diagram of an interlaced scanning method according to embodiment 1;
FIG. 3 is a schematic representation of the Gaussian distribution laser energy and the shape of the weld pool bottom weld line for example 1, (a) is a Gaussian heat source form, (b) is a weld line plot for example 1, (c) is a weld line plot for comparative example 1, (d) is a cross-sectional view of the weld pool for example 1, and (e) is a cross-sectional view of the weld pool for comparative example 1;
FIG. 4 is a plot of columnar-equiaxed transformation for the Inconel 718 alloy;
FIG. 5 is a weave diagram of a vertical cross section of a nickel-base superalloy component prepared by the method of example 1, wherein (a) is a polar diagram, (b) is an inverse polar diagram, (c) is an orientation diagram of coloring of the inverse polar diagram, and (d) is an orientation difference layout;
FIG. 6 is a weave diagram of a horizontal cross section of a nickel-base superalloy component prepared by the method of example 1, wherein (a) is a polar diagram, (b) is an inverse polar diagram, (c) is an orientation diagram of coloring of the inverse polar diagram, and (d) is an orientation difference layout.
Detailed Description
It is to be understood that the following detailed description is exemplary and is intended to provide further explanation of the invention as claimed. Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs.
It is noted that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of example embodiments according to the present application. As used herein, the singular forms "a", "an" and "the" are intended to include the plural forms as well, and it should be understood that when the terms "comprises" and/or "comprising" are used in this specification, they specify the presence of stated features, steps, operations, devices, components, and/or combinations thereof, unless the context clearly indicates otherwise.
In a first aspect, a method for reducing the texture strength of a laser stereolithography superalloy, the method comprising:
selecting a laser with laser energy conforming to Gaussian distribution;
carrying out layer-by-layer melting deposition on the alloy powder flow conveyed by the carrier gas on a metal substrate;
the laser scanning adopts a method of interlamination staggered scanning, and the moving directions of laser melting baths in adjacent deposition layers are different.
Based on the characteristics of point-by-point deposition and layer-by-layer accumulation of the laser stereolithography technology, the texture intensity at any position of a deposition layer can be effectively regulated and controlled. The specific regulation and control method is that the change of the growth direction of the dendrite of each layer is realized through the change of the scanning direction of each layer, so that the strength of the texture is changed, the change of the moving direction of a laser molten pool in an adjacent deposition layer changes the direction of the temperature gradient, and when the change of the direction of the temperature gradient exceeds 45 degrees, the growth direction of the dendrite is changed, for example, the dendrite is turned to the <010> direction or the <100> direction from the <001> direction, so that the formation of the turning dendrite is promoted.
Therefore, in the actual operation process, large laser power (the semiconductor laser power is more than or equal to 4kW) and large beam diameter (generally more than or equal to 5mm) are selected, so that a large-diameter molten pool and a large-curvature molten pool fusion line are formed. The local temperature gradient direction (along the normal direction) of a fusion line at the bottom of the molten pool can be changed, so that the growth direction of dendrites is induced to be changed; according to the relationship between the temperature gradient and the interface migration rate shown in fig. 4, although the value of the temperature gradient still satisfies the epitaxial growth of the columnar crystal, the interlayer staggered scanning manner (i.e., the difference between the scanning directions of two layers is 90 °) causes the direction of the temperature gradient between the layers to change in space, which aggravates the change of the direction of the local temperature gradient, thereby realizing the reduction of the texture strength.
In some embodiments of the invention, the alloy powder is an Inconel 718 alloy powder. The alloy powder is prepared by methods such as an air atomization method or a rotating electrode method.
In some embodiments of the present invention, the alloy substrate is made of Inconel 718 alloy and has a grain size of about 45-55 μm.
In some embodiments of the invention, the diameter of the laser beam is ≧ 5 mm.
In some embodiments of the invention, the power of the laser is 4kW or more.
The diameter of the laser beam is in a larger diameter range, and the laser is in higher power, so that a larger molten pool (larger molten pool diameter and larger molten pool depth) is formed in the laser three-dimensional forming process, and conditions are created for competitive growth of dendrites.
In some embodiments of the present invention, the starting point of each deposition layer is located at the position of the vertex of each deposition layer, and the starting point of each deposition layer sequentially changes in a counterclockwise direction from bottom to top.
In some embodiments of the present invention, the powder feeding rate of the alloy powder is 30g/min or more. The laser with higher power and larger diameter range is adopted for depositing the alloy powder, and the powder feeding rate also adopts a larger range, so that on one hand, good formability can be ensured, on the other hand, the forming efficiency can be improved, and the cost is reduced.
In some embodiments of the present invention, the metal substrate has a length of 100mm or more and a width of 100mm or more. The height of the deposited layer is determined by the dimensions of the particular formed part.
In a second aspect, the method for reducing the texture strength of the laser stereolithography superalloy is applied to the field of laser stereolithography of superalloys.
The invention will be further illustrated by the following examples
Example 1
Adopting a laser stereo forming technology, taking forging-state Inconel 718 alloy as a substrate (the grain size is about 50 mu m), and selecting Inconel 718 alloy powder prepared by an air atomization method or a rotary electrode method as a raw material;
the Inconel 718 alloy substrate has the size of 1600 multiplied by 700 multiplied by 50mm3。
Selecting a laser with laser energy conforming to Gaussian distribution;
carrying out layer-by-layer melting deposition on the alloy powder flow conveyed by the carrier gas on a metal substrate; the powder feeding rate is 30 g/min;
the diameter of a laser beam is 5mm, and the power of the laser is 4 kW;
the laser scanning process adopts an interlayer staggered scanning mode, the number of deposited layers is 1000, the light starting points are positioned at the top points of the cross section of the forming part, and the light starting points of each layer are different.
As shown in the technical roadmap of fig. 1, the shaping method includes changing the characteristics of the laser beam and changing the laser scanning pattern. The control of the solidification conditions is achieved by controlling the forming method.
The laser scanning adopts an interlaminar interleaving mode, and as shown in fig. 2, the scanning direction of each layer is different by 90 degrees. The starting points of all layers are different, namely, the layers are alternately arranged from bottom to top according to the direction of A-B-C-D.
The laser selects a laser having a laser beam characteristic of a gaussian distribution. As shown in fig. 3 a. By using the laser with high power and Gaussian distribution laser beam characteristics, a fusion line with high curvature can be induced in the process of laser three-dimensional forming, and as shown in fig. 3b and 3d, the included angle theta between the normal direction of the fusion line and the vertical direction1When theta is1And when the temperature is more than or equal to 45 ℃, the obtained dendritic crystal morphology of the cross section of the molten pool is a turning dendritic crystal.
Example 2
In comparison with example 1, the Inconel 718 alloy substrate had a size of 160X 70X 20mm3. The number of deposition layers was 100.
Comparative example
Compared with the embodiment, the power of the laser beam adopting the laser is 2kW, the laser energy also conforms to Gaussian distribution, the cross-sectional morphology of the molten pool formed by laser processing is shown in FIGS. 3c and 3e, it can be seen that the local normal directions of the fusion lines are parallel to each other and vertically upward, and the dendritic growth of the molten pool is epitaxial growth along the deposition direction.
In the process of carrying out three-dimensional forming by high-power and Gaussian energy distributed laser, a fusion line with high curvature corresponds to the change of the local temperature gradient direction, and is more beneficial to the competitive growth of dendritic crystals. The high-power laser and the large laser beam diameter can form a large laser molten pool, provide space for dendritic crystal growth at the position of the upper edge of the fusion line and are more beneficial to competitive growth of the dendritic crystal; meanwhile, the large powder feeding rate can improve the deposition efficiency of laser three-dimensional forming and reduce the manufacturing cost of large-scale complex components.
The CET transition curve of the nickel-base superalloy is shown in fig. 4. In fig. 4, the interface migration rate R is 6 × 10-3m/s and R1.5X 10-2m/s. The high power laser reduces the temperature gradient in the melt pool and promotes the formation of equiaxed crystals.
Inter-layer interleaving is used to change the temperature gradient between deposited layers and thus promote the formation of steering dendrites. The solidification condition can be accurately regulated and controlled through the process control of the laser three-dimensional forming method, so that the growth of equiaxial crystals is promoted, the epitaxial growth of columnar crystals is inhibited, the formation of turning dendrites is promoted, and the texture strength of large and complex laser three-dimensional forming components can be effectively reduced.
The texture intensity map of the test piece obtained in example 1 on a vertical cross section is shown in fig. 5. It can be seen that although the columnar crystal still exists, the epitaxial growth characteristic disappears, and only the columnar crystal with small length-width ratio exists in one deposition layer; in addition, a difference occurs in the direction of columnar crystal growth in a molten pool range, i.e., there is a competitive growth. Due to the limited number of statistical grains, the local texture strength is high (MUD 15.70).
The texture strength of the test piece obtained in example 1 in the horizontal section is shown in fig. 6. It can be seen that the texture strength in horizontal section (MUD ═ 3.37) is already close to that of the forging.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (9)
1. A method for reducing the texture strength of laser three-dimensional forming high-temperature alloy is characterized by comprising the following steps: the method comprises the following steps:
selecting a laser with laser energy conforming to Gaussian distribution;
carrying out layer-by-layer melting deposition on the alloy powder flow conveyed by the carrier gas on a metal substrate;
the laser scanning adopts a method of interlamination staggered scanning, and the moving directions of laser melting baths in adjacent deposition layers are different.
2. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the alloy powder is Inconel 718 alloy powder.
3. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the material of the alloy substrate is Inconel 718 alloy, and the grain size is about 45-55 mu m.
4. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the diameter of the laser beam is more than or equal to 5 mm.
5. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the power of the laser is more than or equal to 4 kW.
6. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the starting point of each deposition layer is located at the position of the vertex of each deposition layer, and the starting point of each deposition layer sequentially changes in a counterclockwise direction from bottom to top.
7. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the powder feeding speed of the alloy powder is more than or equal to 30 g/min.
8. The method for reducing the texture strength of the laser stereolithography superalloy as in claim 1, wherein: the length of the metal substrate is more than or equal to 100mm, and the width of the metal substrate is more than or equal to 100 mm.
9. Use of the method for reducing the texture intensity of a laser stereolithography superalloy as claimed in any of claims 1 to 8 in the field of laser stereolithography of superalloys.
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