CN115488353A - SLM (Selective laser melting) forming method of high-temperature alloy material - Google Patents
SLM (Selective laser melting) forming method of high-temperature alloy material Download PDFInfo
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- 238000000034 method Methods 0.000 title claims abstract description 32
- 238000002844 melting Methods 0.000 title claims abstract description 26
- 230000008018 melting Effects 0.000 title claims abstract description 26
- 239000000843 powder Substances 0.000 claims abstract description 73
- 239000000758 substrate Substances 0.000 claims abstract description 54
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 28
- 238000000465 moulding Methods 0.000 claims abstract description 25
- 238000003892 spreading Methods 0.000 claims abstract description 19
- 238000007639 printing Methods 0.000 claims abstract description 17
- 238000001035 drying Methods 0.000 claims abstract description 7
- 239000010935 stainless steel Substances 0.000 claims abstract description 6
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 6
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- 239000010410 layer Substances 0.000 claims description 30
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- 229910000601 superalloy Inorganic materials 0.000 claims description 6
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- 238000010438 heat treatment Methods 0.000 claims description 5
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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
- 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
-
- 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
- B22F10/37—Process control of powder bed aspects, e.g. density
-
- 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
-
- 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
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
- B33Y40/20—Post-treatment, e.g. curing, coating or polishing
-
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0433—Nickel- or cobalt-based alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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- 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
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- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Automation & Control Theory (AREA)
- Crystallography & Structural Chemistry (AREA)
- Plasma & Fusion (AREA)
- Laser Beam Processing (AREA)
Abstract
The invention discloses an SLM (selective laser melting) molding method of a high-temperature alloy material, which comprises the steps of starting laser selective melting molding equipment, and guiding a sliced printing model into a computer operating system; carrying out ultrasonic cleaning and wiping on the surface of the stainless steel substrate, and drying; the method comprises the following steps that preheated high-temperature alloy powder is spread on a substrate by a scraper to form a uniform powder spreading layer, a YAG laser emits continuous Gaussian laser beams, scanning printing is carried out on the powder layer after powder spreading according to a leading-in model and a set program, each layer of scanning adopts a mode of scanning the interior of the model in a partitioning mode and then scanning the outline of the model, the substrate moves downwards according to the powder spreading thickness, and the height of a laser scanning section is kept until printing is finished; and cutting the substrate by using an electric spark, and finally taking down the sample. The invention can obtain a finished product with high density, reduces special forming defects such as incomplete powder melting, air gaps, holes and the like, and improves the quality, the mechanical property and the service time of a part of a forming sample.
Description
Technical Field
The invention relates to a high-temperature alloy material powder forming technology, in particular to an SLM (Selective laser melting) forming method of a high-temperature alloy material.
Background
The laser additive manufacturing technology is an advanced manufacturing technology which can meet the integrated requirements of high performance and high precision forming, has the advantages of integrated forming of complex parts, short production period, product diversification, no cost increase, raw material saving, accurate entity replication and the like, and is a metal powder rapid forming technology which is simpler than a Selective Laser Sintering (SLS) technology process flow.
The high-temperature alloy is an iron-based, nickel-based and cobalt-based metal material which can be used for a long time in a high-temperature environment of more than 600 ℃, bear complex alternating load and has surface stability. The research and application level of the high-temperature alloy is an important mark for measuring the comprehensive strength of scientific development in the national material field.
The cobalt-based high-temperature alloy is particularly suitable for hot end components of advanced power propulsion systems such as turbine engines, ground gas turbines and the like, and GH5188 is commonly used for manufacturing high-temperature components such as inner walls, outer walls, sealing sheets and the like of combustion chambers. When the heavy gas engine turbine blade with a complex shape is processed and manufactured, the number of through holes with uniform and non-uniform special-shaped apertures mostly being 1.5mm distributed on the end wall, the blade surface to the tail edge, the base and two layers of cooling structures inside the blade body exceeds one thousand, and the general cutting and drilling process is complex in operation and huge in workload. The selective laser melting and forming technology adopts a layer-by-layer scanning and forming method, so that the production efficiency is high, and the precision is better. However, the biggest problem faced by the superalloy additive manufacturing forming process is the control of the forming quality, and the scanning strategy design should be dominated by the laser power, the scanning speed, the scanning distance and the interlayer rotation angle which are crucial to the sample forming and the quality thereof. And special forming defects such as incomplete powder melting, air gaps, holes and the like can be generated between adjacent powder laying layers and in a local area of a melting pool in a laser scanning path, so that the quality, the mechanical property and the service safety of parts of a forming sample are influenced.
At present, researchers can not obtain a high-density forming process aiming at selective laser melting once-formed GH5188 high-temperature alloy.
Disclosure of Invention
In view of the above problems, an object of the present invention is to provide a SLM forming method for high temperature alloy materials, which can obtain GH5188 alloy with high density, no macroscopic deformation and crack, and excellent performance in use while forming with high precision.
The object of the invention is thus achieved. A SLM forming method of a high-temperature alloy material comprises the following steps:
1) Preserving the heat of GH5188 high-temperature alloy powder in a vacuum drying oven at 80 ℃ for 4h and drying;
2) Starting laser selective melting forming equipment, guiding the sliced printing model into a computer operating system, setting printing parameters, wherein each layer of partition is in a strip shape, the scanning mode is that the inside is scanned and printed, and the outer contour is scanned and printed after the inside is scanned and printed;
3) Ultrasonically cleaning the surface of a stainless steel substrate for 30min by using a stainless steel cleaning agent, wiping the surface by using absolute ethyl alcohol with the purity of 99 percent, and drying;
4) Installing a substrate in a molding bin of selective laser melting molding equipment, and loading GH5188 high-temperature alloy powder into a powder spreading bin of the selective laser melting molding equipment;
5) Pumping the oxygen content in the molding bin to be below 100ppm, introducing argon with the purity of 99.99 percent for gas washing, and keeping the argon atmosphere in the molding bin to blow the argon in parallel along the surface of the substrate at the flow rate of 3.5-4.5 m/s;
6) Preheating the substrate and GH5188 high-temperature alloy powder to 400 ℃ so as to reduce the temperature difference between the high-temperature alloy powder and the substrate after laser irradiation;
7) Paving powder on the preheated GH5188 high-temperature alloy powder on a substrate by using a scraper to form uniform powder paving layers, wherein the powder paving thickness of each layer is 40 mu m;
8) YAG laser emits continuous Gaussian laser beams, scanning and printing are carried out on the powder layer after powder spreading according to a leading-in model and a set program, and each layer of scanning adopts a mode of scanning the interior of the model in a partitioning mode and then scanning the outline of the model; the power of the Gaussian laser beam is 200-240W, the scanning speed is 400-800mm/s, and the scanning interval is 0.08-0.12mm; and ensuring that the argon is blown through the substrate in parallel;
9) Repeating the step 7) and the step 8), wherein the rotation angle of the laser scanning path in which the layers are staggered is 45-90 degrees, the substrate moves downwards according to the powder spreading thickness, and the laser scanning section height is kept until the printing is finished;
10 Keeping the argon atmosphere in the molding bin after printing is finished, relieving the pressure after the temperature in the molding bin is cooled to be below 50 ℃, opening a bin door, and taking out the printed substrate;
11 Performing stress relief annealing treatment on the printed substrate to eliminate thermal stress generated in the SLM process;
12 Using an electric spark to cut the substrate, and finally taking off the substrate.
Further, the substrate is a 304 stainless steel plate.
Further, the GH5188 high-temperature alloy powder comprises the following components in percentage by mass: 23.17% of Ni,23.13% of Cr,13.58% of W,1.26% of Fe,0.39% of Si,0.03% of La,0.07% of C,0.02% of Cu, and the balance of Co.
Further, the selective laser melting forming device is a BLT-S210-X rapid forming system.
Further, the operating system of the computer is SliceViewer V3.85.
Further, the laser power of the Gaussian laser beam is 200W, the scanning speed is 800mm/s, and the scanning interval is 0.08mm.
Furthermore, the rotation angle of the laser scanning path in the staggered mode between layers is 45 degrees, interlayer fusion is facilitated, and the condition that a molten pool in an X-Z plane area of the longitudinal section is overlapped to form a fish scale-shaped appearance is reduced.
Further, the stress relief annealing treatment comprises the following steps:
1) Heating from normal temperature for 80 minutes to 400 ℃;
2) Keeping the temperature at 400 ℃ for 10 minutes;
3) Heating again for 112 minutes to 960 deg.C;
4) Preserving the heat for 10 minutes;
5) Water quenching to 600 ℃;
6) And air-cooling to room temperature.
According to the invention, through adjusting the laser power, the scanning speed, the scanning interval and the powder spreading thickness, a proper laser energy density is found, so that the powder is fully melted and formed, and the generation of forming defects such as holes and cracks is favorably reduced; the sectional scanning is adopted to help heat to be uniformly dispersed and radiated, the thermal deformation caused by overhigh local temperature is avoided, the surface quality is improved by scanning the outline of the sample, and the sample processed by using the process parameter has high forming density, so that a finished product with high density is obtained, some special forming defects such as incomplete powder melting, air gaps, holes and the like are reduced, and the quality, the mechanical property and the service time of a formed sample are improved.
Drawings
FIG. 1 is a block diagram of a selective laser melting apparatus for use in the method of the present invention;
FIG. 2 is a drawing of a high-temperature alloy forming sample with 98.54% compactness obtained in example 1 of the invention;
FIG. 3 is a diagram of a formed sample of a superalloy with a density of 98.73% obtained in example 2 of the present invention;
FIG. 4 is a drawing of a high-temperature alloy forming sample with 98.49% of compactness obtained in example 3 of the invention;
in the figure: 1. the laser comprises a computer, a 2 YAG laser, a 3 forming bin, a 4 scraper, a 5 forming piece, a 6 base plate, a 7 powder spreading bin, 8 high-temperature alloy powder and 9 laser beams.
Detailed Description
The invention is further illustrated by the following examples in conjunction with the drawings. Referring to fig. 1, the selective laser melting and forming device (BLT-S210-X rapid forming system) of the present invention is formed by connecting a computer 1 to a YAG laser 2, wherein a forming chamber 3 is installed below the YAG laser 2, the forming chamber 3 is provided with an air inlet and an air outlet, a powder spreading chamber 7 is installed below one side of the air inlet in the forming chamber 3, GH5188 high temperature alloy powder 8 is installed in the powder spreading chamber 7, a scraper 4 is installed at the opening of the powder spreading chamber 7, the air outlet is installed outside a laser beam 9 of the YAG laser 2, a substrate 6 is installed below the YAG laser 2, and a formed part 5 is installed above the substrate 6. The GH5188 high-temperature alloy powder 8 used in the invention comprises the following components in percentage by mass: 23.17% of Ni,23.13% of Cr,13.58% of W,1.26% of Fe,0.39% of Si,0.03% of La,0.07% of C,0.02% of Cu, and the balance of Co, with stable performance and good effect.
Example 1:
an SLM method of a superalloy material, comprising the steps of:
1) Preserving the heat of the GH5188 high-temperature alloy powder 8 in a vacuum drying oven at 80 ℃ for 4h and drying;
2) Starting laser selective melting forming equipment (BLT-S210-X rapid forming system), guiding the sliced printing model into an operating system (SliceViewer V3.85) of the computer 1, setting printing parameters, wherein each layer of partition is in a strip shape, the scanning mode is that the inside is scanned and printed firstly, and the outer contour is scanned and printed after the inside is scanned and finished;
3) Ultrasonically cleaning the surface of the stainless steel substrate 6 for 30min by using a stainless steel cleaning agent, wiping by using absolute ethyl alcohol with the purity of 99 percent, and drying;
4) Installing a substrate 6 in a forming bin 3 of the selective laser melting forming equipment, and loading GH5188 high-temperature alloy powder 8 into a powder spreading bin 7 of the selective laser melting forming equipment;
5) Pumping the oxygen content in the molding bin 3 to be below 100ppm, introducing argon with the purity of 99.99 percent for gas scrubbing, keeping the argon atmosphere in the molding bin 3, and blowing the argon at the flow rate of 3.5m/s along the surface of the substrate 6 in parallel;
6) Preheating the substrate 6 and GH5188 high-temperature alloy powder 8 to 400 ℃;
7) Paving preheated GH5188 high-temperature alloy powder 8 on a substrate 6 by using a scraper 4 to form uniform powder paving layers, wherein the powder paving thickness of each layer is 40 mu m;
8) YAG laser 2 emits continuous Gaussian laser beam 9 to scan and print on the powder layer after powder spreading according to a leading-in model and a set program, and each layer of scanning adopts a mode of scanning the interior of the model in a subarea mode and then scanning the outline of the model; the power of the Gaussian laser beam 9 is 200W, the scanning speed is 600mm/s, and the scanning interval is 0.08mm; and to ensure that argon is blown parallel to the substrate 6;
9) Repeating the step 7) and the step 8), wherein the interlayer rotation angle of the laser scanning path is 67 degrees, the substrate 6 moves downwards according to the powder laying thickness, and the laser scanning section height is kept until the printing is finished;
10 Keeping the argon atmosphere in the molding bin 3 after the printing is finished, releasing the pressure after the temperature in the molding bin 3 is cooled to be below 50 ℃, opening a bin door, and taking out the printed substrate 6;
11 Stress relief annealing treatment is carried out on the printed substrate 6 to eliminate thermal stress generated in the SLM process;
12 The substrate 6 is cut into a sample by an electric spark, and the sample 5 is removed.
The resulting test piece had dimensions of 10 mm. Times.10 mm, a sample density of 98.54%, a roughness of 13.5 μm, and a hardness of 284.67HV (as shown in FIG. 2).
Example 2:
an SLM method of a high-temperature alloy material comprises the following steps 5) and 8):
5) Pumping the oxygen content in the molding bin 3 to be below 100ppm, introducing argon with the purity of 99.99 percent for gas scrubbing, keeping the argon atmosphere in the molding bin 3, and blowing the argon at the flow rate of 4.0m/s along the surface of the substrate 6 in parallel;
8) YAG laser 2 emits continuous Gaussian laser beam 9 to scan and print on the powder layer after powder spreading according to a leading-in model and a set program, and each layer of scanning adopts a mode of scanning the interior of the model in a subarea mode and then scanning the outline of the model; the power of the Gaussian laser beam 9 is 200W, the scanning speed is 800mm/s, and the scanning interval is 0.08mm; and ensures that argon is blown parallel to the substrate 6.
The rest is the same as in example 1.
The resulting test piece had dimensions of 10 mm. Times.10 mm, a sample density of 98.73%, a roughness of 11.7 μm, and a hardness of 298.28HV (as shown in FIG. 3).
Example 3:
the SLM method of the high-temperature alloy material comprises the following steps of 5) and 8):
5) Pumping the oxygen content in the molding bin 3 to be below 100ppm, introducing argon with the purity of 99.99 percent for gas washing, and keeping the argon atmosphere in the molding bin 3 to blow the argon in parallel along the surface of the substrate 6 at the flow rate of 4.5 m/s;
8) YAG laser 2 emits continuous Gaussian laser beam 9 to scan and print on the powder layer after powder spreading according to a leading-in model and a set program, and each layer of scanning adopts a mode of scanning the interior of the model in a subarea mode and then scanning the outline of the model; the power of the Gaussian laser beam 9 is 240W, the scanning speed is 600mm/s, and the scanning interval is 0.10mm; and ensures that argon is blown parallel to the substrate 6.
The rest is the same as in example 1.
The resulting test piece had a molded size of 10 mm. Times.10 mm, a sample density of 98.49%, a roughness of 15.9 μm, and a hardness of 285.78HV (as shown in FIG. 4).
By comparison of the above examples, the samples of examples 1, 2 and 3 all have a density of over 98%, and a hardness of over 280HV, which is better, and example 2 has the highest density, the highest hardness, the lowest roughness and the best molding effect.
The SLM forming method cleans the surface of the substrate by using a cleaning agent, removes dust, oil stains and other dirt on the surface, and avoids influencing the shape of a formed piece; vacuumizing the forming cavity, filling protective gas (argon) which is blown in parallel along the surface of the substrate, wherein the flow rate of the protective gas is 3.5-4.5m/s, so that the generation of oxidation is prevented, and small particles can be blown off from the surface of the formed layer in a splashing manner, thereby reducing defects; preheating the substrate, reducing the temperature difference between laser irradiation powder and the substrate, and avoiding warping and infirm bonding caused by thermal stress; the GH5188 powder is preheated, the preheating temperature corresponds to the preheating temperature of the substrate, the temperature difference between the laser irradiation powder and the substrate powder is reduced, and the generation of forming defects is reduced; the preheated high-temperature alloy powder is spread on a substrate to form single-layer spread powder, and the powder is spread uniformly; scanning the profile of the cross section by using laser, scanning the interior of each layer by adopting partition scanning, then scanning the profile, wherein the laser power is 200W, the scanning speed is 800mm/s, the scanning interval is 0.08mm, and the protective gas is blown out in parallel to the substrate; when the laser power is lower, a large amount of powder appears in a metallographic structure, the powder is not completely melted, holes and cracks with larger sizes are formed, the holes and the cracks are reduced along with the increase of the laser power, when the laser power is higher, the laser heat and force are overlarge, so that severe splashing is caused, and the heat dissipation of a sample is difficult to cause thermal deformation; the size of the scanning speed significantly affects the size and distribution of holes and cracks. The X-Z plane of the formed part can be seen from a scanning path melting channel, and a molten pool in the X-Z plane area of the longitudinal section is overlapped to form a fish scale-shaped appearance; by adjusting the laser power, the scanning speed, the scanning interval and the powder spreading thickness, a proper laser energy density is found, so that the powder is fully melted and formed, and the generation of forming defects (holes and cracks) is reduced; the partition scanning is beneficial to uniformly dispersing and dissipating heat of heat, avoids thermal deformation caused by overhigh local temperature, finally scans the outline of the sample and improves the surface quality, and the sample formed by processing the process parameter has high forming density; the scanning path adopts staggered scanning between layers until the forming is finished, the substrate moves downwards according to the powder laying thickness, the height of the laser scanning section is kept constant, and a product is formed according to the design requirement; and carrying out heat treatment on the formed product, wherein the annealing process can eliminate the internal stress generated in the SLM process and improve the performance of the sample. The finished product with high density can be obtained, the special forming defects such as incomplete powder melting, air gaps, holes and the like are reduced, and the quality, the mechanical property and the service time of a forming sample piece are improved.
Claims (8)
1. An SLM method of a high-temperature alloy material is characterized by comprising the following steps:
1) Preserving the heat of the GH5188 high-temperature alloy powder in a vacuum drying oven at 80 ℃ for 4h and drying;
2) Starting selective laser melting forming equipment, importing the sliced printing model into a computer operating system, setting printing parameters, wherein each layer of partition is in a strip shape, and the scanning mode is that the inside is scanned and printed firstly, and the outer contour is scanned and printed after the inside is scanned and printed;
3) Ultrasonically cleaning the surface of the substrate for 30min by using a stainless steel cleaning agent, wiping the surface by using absolute ethyl alcohol with the purity of 99 percent, and drying;
4) Installing a substrate in a molding bin of selective laser melting molding equipment, and loading GH5188 high-temperature alloy powder into a powder spreading bin of the selective laser melting molding equipment;
5) Pumping the oxygen content in the molding bin to be below 100ppm, introducing argon with the purity of 99.99 percent for gas scrubbing, and keeping the argon atmosphere in the molding bin to blow the argon at the flow rate of 3.5-4.5m/s in parallel along the surface of the substrate;
6) Preheating the substrate and GH5188 high-temperature alloy powder to 400 ℃ so as to reduce the temperature difference between the high-temperature alloy powder and the substrate after laser irradiation;
7) Paving powder on the preheated GH5188 high-temperature alloy powder on a substrate by using a scraper to form uniform powder paving layers, wherein the powder paving thickness of each layer is 40 mu m;
8) YAG laser emits continuous Gaussian laser beams, scanning and printing are carried out on the powder layer after powder spreading according to a leading-in model and a set program, and each layer of scanning adopts a mode of scanning the interior of the model in a partitioning mode and then scanning the outline of the model; the power of the Gaussian laser beam is 200-240W, the scanning speed is 400-800mm/s, and the scanning interval is 0.08-0.12mm; and ensuring that the argon is blown through the substrate in parallel;
9) Repeating the step 7) and the step 8), wherein the rotation angle of the laser scanning path in which the layers are staggered is 45-90 degrees, the substrate moves downwards according to the powder spreading thickness, and the laser scanning section height is kept until the printing is finished;
10 Keeping the argon atmosphere in the molding bin after printing is finished, relieving the pressure after the temperature in the molding bin is cooled to be below 50 ℃, opening a bin door, and taking out the printed substrate;
11 Performing stress relief annealing treatment on the printed substrate to eliminate thermal stress generated in the SLM process;
12 Cutting the substrate by using an electric spark, and finally removing the sample.
2. The SLM method for a superalloy material according to claim 1, wherein the substrate is a 304 stainless steel plate.
3. The SLM method of the high-temperature alloy material, according to the claim 1, characterized in that the composition and mass percentage of the GH5188 high-temperature alloy powder are as follows: 23.17% Ni,23.13% by weight, 13.58% by weight, 1.26% by weight of Fe,0.39% by weight of Si,0.03% by weight of La,0.07% by weight of C,0.02% by weight of Cu, the balance being Co.
4. The SLM method for high temperature alloy materials claimed in claim 1, characterized in that the laser selective melting shaping device is a BLT-S210-X rapid shaping system.
5. The SLM method for a superalloy material as claimed in claim 1, wherein the operating system of the computer is SliceViewer V3.85.
6. The SLM method of claim 1, characterized in that the Gaussian laser beam has a laser power of 200W, a scanning speed of 800mm/s and a scanning pitch of 0.08mm.
7. The SLM method of claim 1, characterized in that the laser scanning path is staggered from layer to layer by a rotation angle of 45 ° to facilitate interlayer fusion and reduce the formation of fish scales by overlapping of the molten pool in the X-Z plane area of the longitudinal section.
8. The SLM method for superalloy materials according to claim 1, wherein the stress relief annealing step is as follows:
1) Heating from normal temperature for 80 minutes to 400 ℃;
2) Keeping the temperature at 400 ℃ for 10 minutes;
3) Heating again for 112 minutes to 960 ℃;
4) Preserving the temperature for 10 minutes;
5) Water quenching to 600 ℃;
6) And air-cooling to room temperature.
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