CN113996813A - Nickel-based alloy part and preparation method thereof - Google Patents
Nickel-based alloy part and preparation method thereof Download PDFInfo
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- CN113996813A CN113996813A CN202111324361.8A CN202111324361A CN113996813A CN 113996813 A CN113996813 A CN 113996813A CN 202111324361 A CN202111324361 A CN 202111324361A CN 113996813 A CN113996813 A CN 113996813A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
- B33Y40/20—Post-treatment, e.g. curing, coating or polishing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- 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
- 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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
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- 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
Abstract
The invention discloses a nickel-based alloy part and a preparation method thereof, relating to the technical field of nickel-based alloy parts for aerospace, wherein the method comprises the steps of obtaining a 3D printing alloy part; carrying out solid solution treatment on the 3D printed alloy piece to obtain a solid solution alloy piece; heating the solid solution alloy piece, and carrying out first time effect treatment, wherein in the first time effect treatment, the heating temperature is less than or equal to 730 ℃, and the heating time is more than or equal to 7 h; and carrying out first cooling, heat preservation and second cooling on the first time effect alloy piece to carry out second time effect treatment to obtain the nickel-based alloy piece, wherein in the second time effect treatment, the first cooling finishing temperature is 605-. By adopting the method provided by the invention, the tensile strength of the nickel-based alloy piece is 1450-1489MPa, the yield strength is 1327-1360MPa, the elongation is 18.8-20.5 percent, and the impact energy is 63-67J under the normal temperature condition; at the temperature of 650 ℃, the tensile strength is 1120-1130MPa, the yield strength is 960-978MPa, the elongation is 14.9-16.2%, the strength is high, the toughness is good, and no cracking risk exists.
Description
Technical Field
The invention belongs to the technical field of nickel-based alloy parts for aerospace, and particularly relates to a nickel-based alloy part and a preparation method thereof.
Background
The nickel-based alloy is prepared by a selective laser melting forming technology, can realize the integral forming of complex parts in one step, has better performance after heat treatment, thereby meeting more rigorous service environment, and can be used as a core material of an aerospace structural member and a part in an aircraft.
At present, the nickel-based alloy parts prepared by adopting GH4169 powder and GH4099 powder as raw materials through a 3D printing technology have good strength and plasticity, but have poor toughness and internal cracking risk.
Disclosure of Invention
In order to solve the technical problems, the invention provides the preparation method of the nickel-based alloy part, and the alloy part prepared by the method has good strength, plasticity and toughness at high temperature and small cracking risk.
The technical scheme of the invention is as follows:
in one aspect, the present disclosure provides a method of making a nickel-based alloy part, the method comprising:
obtaining a 3D printing alloy piece;
carrying out solid solution treatment on the 3D printed alloy piece to obtain a solid solution alloy piece;
heating the solid solution alloy piece, and carrying out first time effect treatment, wherein in the first time effect treatment, the heating temperature is less than or equal to 730 ℃, and the heating time is more than or equal to 7 h;
and carrying out first cooling, heat preservation and second cooling on the first time effect alloy piece to carry out second time effect treatment to obtain the nickel-based alloy piece, wherein in the second time effect treatment, the first cooling finishing temperature is 605-.
Further, in the first time-effect treatment, the heating temperature is 710-.
Further, in the second aging process, the second cooling end temperature is 20-80 ℃.
Further, the solution treatment comprises the steps of heating the 3D printing alloy piece to 1100 +/-10 ℃ in three stages, keeping the temperature for 1-2h, and cooling at the rate of 130-160 ℃/s.
Further, in the solution treatment process, the vacuum degree is 0.1-10 Pa.
Further, in the solution treatment process, the cooling finishing temperature is 20-80 ℃.
Further, the three-stage heating comprises a first heating, a second heating and a third heating, wherein in the first heating, the heating temperature is 490-510 ℃, the heat preservation time is 30-40min, and the heating rate is 7-10 ℃/min; in the second heating, the heating temperature is 810-; in the third heating, the heating temperature is 1090-1110 ℃, the heat preservation time is 1-2h, and the heating rate is 5-8 ℃/min.
Further, in the solid solution treatment, the cooling is oil cooling, the temperature of oil used for the oil cooling is 20-80 ℃, and the cooling time is 20-30 min.
Further, the obtaining of the 3D printing alloy piece comprises,
obtaining a printing program of the alloy piece;
3D laser printing is carried out on the alloy powder according to the printing program to obtain a blank piece; the alloy powder is any one of the following: GH4169 powder, GH4099 powder; the particle size of the alloy powder is 30-55 microns, in the 3D laser printing process, the laser power is 200-400W, the scanning speed is 800-1200 mm/s, the powder spreading layer thickness is 40-60 microns, the laser lapping interval is 0.6-1.2 mm, the light spot compensation is 0.07-0.12 mm, and the substrate thickness is 35-45 mm;
and performing powder cleaning treatment on the blank piece to obtain a 3D printing alloy piece.
On the other hand, the invention provides a nickel-based alloy piece which is prepared by the preparation method of the nickel-based alloy piece.
The beneficial effects of the invention at least comprise:
according to the nickel-based alloy part and the preparation method thereof provided by the invention, Fe and Cr are dissolved in a nickel-based matrix in a solid solution manner, so that the strength of the alloy part is improved, the element segregation is reduced, and the tissue uniformity of the nickel-based alloy part is improved; through the aging treatment and the control of the technological parameters in the aging treatment process, the precipitation of precipitates can be induced, so that the grain boundary strength is improved, and the high-temperature strength and the high-temperature toughness of the material are improved. By adopting the method provided by the invention, the tensile strength of the nickel-based alloy piece is 1450-1489MPa, the yield strength is 1327-1360MPa, the elongation is 18.8-20.5 percent, and the impact energy is 63-67J under the normal temperature condition; at the temperature of 650 ℃, the tensile strength is 1120-1130MPa, the yield strength is 960-978MPa, the elongation is 14.9-16.2%, the strength is high, the toughness is good, and no cracking risk exists.
Drawings
FIG. 1 is a process diagram of a method for manufacturing a nickel-based alloy part according to an embodiment of the invention;
FIG. 2 is a metallographic structure of an alloy member according to example 2;
FIG. 3 is a metallographic structure of an alloy member according to example 3.
Detailed Description
In order to make the present application more clearly understood by those skilled in the art to which the present application pertains, the following detailed description of the present application is made with reference to the accompanying drawings by way of specific embodiments.
The embodiment of the invention provides a preparation method of a nickel-based alloy piece, fig. 1 is an index method process diagram of the nickel-based alloy piece provided by the embodiment of the invention, and with reference to fig. 1, the method comprises the following steps:
s1, obtaining a 3D printing alloy piece;
further, the obtaining of the 3D printed alloy piece includes:
s101, obtaining a printing program of the alloy piece;
s102, carrying out 3D laser printing on the alloy powder according to the printing program to obtain a blank piece;
as an implementation mode of the embodiment of the invention, the particle size of the alloy powder is 30-55 μm, the laser power is 200-400W, the scanning rate is 800-1200 mm/s, the powder spreading layer is 40-60 μm thick, the laser lapping interval is 0.6-1.2 mm, the spot compensation is 0.07-0.12 mm, and the substrate thickness is 35-45 mm in the 3D laser printing process.
As an implementation manner of the embodiment of the invention, the powder cleaning treatment comprises compressed air blowing and ultrasonic cleaning, the pressure of the compressed air is 2-6 MPa, the blowing time is 5-20 min, and the ultrasonic cleaning time is 3-10 min.
S103, performing powder cleaning treatment on the blank to obtain a 3D printing alloy piece, wherein the alloy powder can be any one of the following materials: GH4169 powder and GH4099 powder.
S2, carrying out solid solution treatment on the 3D printed alloy piece to obtain a solid solution alloy piece;
further, the solution treatment comprises the steps of heating the 3D printing alloy piece to 1100 +/-10 ℃ in three stages, keeping the temperature for 1-2h, and cooling at the rate of 130-160 ℃/s.
The selective laser melting, namely the 3D printing process has the characteristics of large temperature gradient, high cooling speed and repeated thermal cycle, so that the nickel-based high-temperature alloy in the printing process is easy to have large internal stress, and microcracks are easy to appear in the nickel-based high-temperature alloy, the high-temperature performance of the alloy part is influenced, the heating temperature is controlled to be 1100 +/-10 ℃, the excessive phase is fully dissolved in the solid solution, the internal stress generated by 3D printing is eliminated, cracks are avoided, the heating temperature is too high, crystal grains can become large and large, and the strength, plasticity and toughness of the alloy part are reduced; the heating temperature is too low, so that the excessive phase is not dissolved enough, and the internal stress is difficult to remove; the heat preservation time is too long, so that the growth of crystal grains is facilitated, coarse crystal grains are formed, and the strength, the plasticity and the toughness of the alloy part are reduced; the heat preservation time is too short, so that the excessive phase cannot be completely dissolved, internal stress still remains, and cracks are easy to appear. The cooling rate is too big, forms quenching stress in the alloy spare easily, and the easy fracture problem appears in the alloy spare, and the cooling rate undersize leads to solid solution element to separate out too much into the phase easily, separates out thick and inhomogeneous distribution in grain boundary department of phase, easily takes place along the crystalline fracture, and then leads to the decline of tensile strength and plasticity.
As an implementation mode of the embodiment of the invention, in the solution treatment process, the vacuum degree is 0.1-10 Pa.
The solution treatment under vacuum condition is used for preventing the alloy part from being oxidized at high temperature.
As an implementation mode of the embodiment of the invention, the cooling ending temperature in the solution treatment process is 20-80 ℃.
The cooling finishing temperature is too high, and the alloy piece is exposed in the air and is easily oxidized, so that the apparent quality is influenced; the cooling finishing temperature is too low, quenching stress is easily formed in the alloy part, and the alloy part is easy to crack.
As an implementation manner of the embodiment of the invention, the three-stage heating includes a first heating, a second heating and a third heating, in the first heating, the heating temperature is 490-510 ℃, the heat preservation time is 30-40min, and the heating rate is 7-10 ℃/min; in the second heating, the heating temperature is 810-; in the third heating, the heating temperature is 1100 +/-10 ℃, the heat preservation time is 1-2h, and the heating rate is 5-8 ℃/min.
The three-stage heating control function is to uniformly heat the inside and the outside of the alloy part to reach the consistent temperature, so that the temperature in the furnace is uniform and consistent, and the excess phases with different solidification temperatures in the 3D printing process can be fully dissolved in the solid solution to achieve the solid solution strengthening function. The first heating temperature is too high, the crystal grains are coarse, and the strength, plasticity and toughness of the alloy part are reduced; the first heating temperature is too low, the interior of the product is not heated sufficiently, and the performance of the product is influenced; the heat preservation time in the first heating process is too long, and crystal grains have enough time to grow, so that the crystal grains are coarse, and the strength, the plasticity and the toughness of the alloy part are reduced; the heat preservation time in the first heating process is too short, the temperature of the alloy part is uneven, and the strength of the alloy part is reduced. The second heating temperature is too high, so that the excessive phase at the solidification temperature can be fully dissolved in the solid solution, the heat preservation time in the second heating process is too long, the crystal grains of the alloy part are easily coarsened, and the strength, the plasticity and the toughness of the alloy part are reduced; the heat preservation time in the second heating process is too short, the excessive phase with the second heating temperature being the solidification temperature is not fully dissolved, and the strength of the alloy part is reduced; the third heating temperature enables the excess phase to be fully dissolved in the solid solution, the 3D printing internal stress is eliminated, cracks are avoided, the third heating temperature is too high, the heat preservation time is too long, crystal grains can become large and large, and the strength, plasticity and toughness of the alloy part are reduced; the third heating temperature is too low, and the holding time is too short, so that the excessive phase is not dissolved.
As an implementation manner of the embodiment of the invention, the cooling is oil cooling, the temperature of oil used for the oil cooling is 20-80 ℃, and the cooling time is 20-30 min.
The temperature of oil used for oil cooling is too high, the cooling time is too long, supersaturated solid solution is difficult to form, subsequent aging treatment is not facilitated, the temperature of oil used for oil cooling is too low, the cooling time is too short, quenching stress is easy to occur, and the alloy part is cracked;
s3, heating the solid solution alloy piece, and carrying out first time effect treatment to obtain a first time effect alloy piece, wherein in the first time effect treatment, the heating temperature is less than or equal to 730 ℃, and the heating time is more than or equal to 7 h;
by aging treatment, a strengthening phase can be fully and uniformly precipitated in the alloy piece, so that the strength, the plasticity and the toughness of the alloy piece are improved. The heating temperature in the aging treatment is too high, crystal grains of the alloy piece are easily coarsened, and precipitates are dissolved and aggregated again, so that the tensile strength of the alloy piece is reduced. The heat preservation time in the aging treatment is too short, the precipitated phase is less, and the pinning dislocation capability is reduced, so that the tensile strength and the plasticity of the material are reduced.
As an implementation manner of the embodiment of the invention, in the first time-effect treatment, the heating temperature is 710-.
In the first time-effect treatment, the heating temperature is too low, so that the precipitation of a strengthening phase is not facilitated, the pinning dislocation capacity is reduced, and the mechanical property is reduced; in the first time-effect treatment, the heat preservation time is too long, the precipitated strengthening phase grows and polymerizes, the distribution of the precipitated strengthening phase is uneven, the quantity of the precipitated strengthening phase is insufficient, and the strength of the alloy part is reduced.
S4, performing first cooling, heat preservation and second cooling on the first time effect alloy piece to perform second time effect treatment to obtain the nickel-based alloy piece, wherein in the second time effect treatment, the first cooling finishing temperature is 605-
The first cooling finishing temperature in the second aging treatment is too high, the second aging treatment is carried out in the air, natural aging is continued, precipitated phases are increased and easy to gather, and the improvement of plasticity is not facilitated; the first cooling finishing temperature in the second aging treatment is too low, residual stress easily exists in the material, and the risk of cracking exists; the heat preservation time in the second aging treatment is too long, precipitated phases grow and are polymerized, and the edgewise fracture is easy to occur, so that the tensile strength and the plasticity are reduced; the heat preservation time in the second aging treatment is too short, which is not beneficial to the precipitation of a strengthening phase, and the pinning dislocation capability is reduced, so that the mechanical property is reduced.
As an implementation manner of the embodiment of the present invention, in the second aging process, the second cooling end temperature is 20 to 80 ℃.
In the second aging treatment, the second cooling rate is too high, and internal stress exists in the alloy part, so that the alloy part is easy to crack; the second cooling rate is too low, and the precipitated strengthening phase is too much and coarsened, which reduces the strength and plasticity of the alloy part.
The following will describe the preparation method of the nickel-based alloy piece provided by the invention in detail with reference to specific examples.
Example 1
In the embodiment, GH4169 material is adopted, LiM-X260A laser selective melting forming equipment of Xin precision company in China is selected to manufacture the folding air vane skeleton, and the enveloping dimension of the part is about 220X 200X 50 mm.
The process for manufacturing the framework comprises the following steps:
(1) optimizing a three-dimensional model and designing allowance based on a complex inner cavity structure of a part and the ultimate forming capability of a selective laser melting forming technology, rotating the model by 50 degrees by UG software to enable the bottom and a substrate to form an included angle of 50 degrees, reducing the supporting amount, adding the allowance between 0.5 and 1.5mm, and adding a furnace metallographic specimen and a tensile test rod;
(2) exporting the three-dimensional model in the step 1 in an STL format, importing the three-dimensional model into Magics software, and carrying out slicing treatment, wherein the process parameters are as follows: layer thickness 40 μm, laser power 280W, scanning speed 940mm/s, lapping 0.8mm, spot compensation 0.12mm, substrate thickness 40mm, shielding gas: and argon gas. And after the slicing is successful, guiding the slices into equipment for blank forming.
(3) And (3) vibrating the blank to clear powder, clearing powder for 10min by using 3MPa compressed air, and then ultrasonically cleaning for 7 min.
(4) And (3) carrying out heat treatment on the blank in the step (3) within 36h, wherein the heat treatment comprises the following steps of solution treatment and aging treatment which are sequentially arranged:
solution treatment: vacuumizing a heating chamber, raising the temperature until the vacuum degree is stabilized below 6.7Pa, raising the temperature to 500 ℃ along with the furnace at the speed of 7 ℃/min, preserving the temperature for 30min, continuing to raise the temperature to 820 ℃, raising the temperature at the speed of 6 ℃/min, preserving the temperature for 30min, simultaneously continuing to raise the temperature to 1100 ℃, raising the temperature at the speed of 6 ℃/min, preserving the temperature for 2h, controlling the vacuum degree in the heating and heat preservation period to be within the range of 0.1 Pa-10.0 Pa, then putting the heating chamber into oil at the temperature of 25 ℃, cooling the heating chamber for 25min, and then air cooling the heating chamber to the room temperature;
aging treatment: heating to 720 ℃, preserving heat for 8 hours, and keeping the vacuum degree within the range of 0.1-10.0 Pa in the heating and heat preserving process; cooling to 620 ℃ along with the furnace within 2h, and preserving heat for 8 h; placing into 35 deg.C oil, oil cooling for 30min, and air cooling to room temperature.
(5) And (4) after the blank piece treated in the step (4) and the substrate are subjected to linear cutting separation, polishing the inner flow channel and the cavity for three times by sequentially adopting 50-80 meshes, 150-180 meshes and 400-450 meshes of abrasive materials, and ensuring that the pressure of the inner cavity is within the range of 1.5-2 MPa.
(6) And (5) machining the blank processed in the step (5) on a 5-axis machine tool, performing three-dimensional finish machining and forming, and then performing liquid sand blasting treatment to finally form the complex inner cavity structure framework.
(7) And carrying out structure observation and mechanical property test on the metallurgical phase and the tensile sample along with the furnace.
Example 2
In the embodiment, GH4169 material is adopted, LiM-X260A laser selective melting forming equipment of Xin precision company in China is adopted to manufacture the outlet flange plate, and the enveloping dimension of the part is about phi 120 multiplied by 100 multiplied by 150 mm.
The manufacturing process of the outlet flange plate comprises the following steps:
(1) optimizing the three-dimensional model, designing allowance, and adding a furnace metallographic specimen and a tensile test bar;
(2) exporting the three-dimensional model in the step 1 in an STL format, importing the three-dimensional model into Magics software, and carrying out slicing treatment, wherein the process parameters are as follows: layer thickness is 40 μm, laser power is 290W, scanning speed is 1000mm/s, lapping interval is 1.0mm, light spot compensation is 0.10mm, substrate thickness is 35mm, protective gas: and argon gas. And after the slicing is successful, guiding the slices into equipment for blank forming.
(3) Cleaning the blank piece with 3MPa compressed air for 5min, and then ultrasonically cleaning for 3 min.
(4) And (4) carrying out heat treatment on the blank piece treated in the step (3) within 36h, wherein the heat treatment comprises solution treatment and aging treatment which are sequentially arranged.
Solution treatment: and vacuumizing the heating chamber, raising the temperature to 490 ℃ along with the furnace at the speed of 8 ℃/min, keeping the temperature for 35min, raising the temperature to 820 ℃ at the speed of 6 ℃/min, keeping the temperature for 40min, raising the temperature to 1100 ℃ at the speed of 6 ℃/min, keeping the temperature for 1.5h, and controlling the vacuum degree in the heating and heat-preservation periods within the range of 0.1-10.0 Pa. Cooling in 35 deg.C oil for 30min, and air cooling to room temperature;
aging treatment: keeping the temperature at 720 ℃ for 8h, and keeping the vacuum degree within the range of 0.1-10.0 Pa in the temperature rising and keeping process; cooling to 620 ℃ along with the furnace within 1.5h, and preserving heat for 7 h; cooling in 40 deg.C oil for 20min, and cooling to room temperature.
(5) The blank processed after step 4 is separated from the substrate by wire cutting.
(6) And (5) machining the blank processed in the step (5) on a 3-axis machine tool, performing three-dimensional finish machining and forming, and then performing liquid sand blasting treatment to finally form the part.
(7) And carrying out structure observation and mechanical property test on the metallurgical phase and the tensile sample along with the furnace.
Example 3
In the embodiment, GH4169 material is adopted, LiM-X260A laser selective melting forming equipment of Xin precision company in China is adopted to manufacture the elbow, and the enveloping dimension of the part is about 220X 150X 50 mm.
The elbow is manufactured by the following process steps:
(1) optimizing a three-dimensional model and designing allowance based on the special structure of a part and the extreme forming capability of a selective laser melting forming technology, rotating the model by 45 degrees by utilizing UG software to reduce the supporting amount, adding the allowance between 0.5 and 1.0mm, and adding a furnace metallographic sample and a tensile test bar;
(2) exporting the three-dimensional model in the step 1 in an STL format, importing the three-dimensional model into Magics software, and carrying out slicing treatment, wherein the process parameters are as follows: layer thickness 40 μm, laser power 285W, scanning speed 970mm/s, overlap joint 1.0mm, spot compensation 0.08mm, substrate thickness 35mm, shielding gas: and argon gas. And after the slicing is successful, guiding the slices into equipment for blank forming.
(3) And (3) performing powder cleaning on the blank piece for 7min by using 3MPa compressed air, and then performing ultrasonic cleaning for 5 min.
(4) And (4) carrying out heat treatment on the workpiece treated in the step (3) within 36h, wherein the heat treatment comprises solution treatment and aging treatment which are sequentially arranged.
Solution treatment: vacuumizing the heating chamber, raising the temperature to 500 ℃ along with the furnace at the speed of 10 ℃/min, keeping the temperature for 30min, continuing to raise the temperature to 810 ℃, raising the temperature at the speed of 7 ℃/min, keeping the temperature for 40min, simultaneously continuing to raise the temperature to 1110 ℃, raising the temperature at the speed of 5 ℃/min, keeping the temperature for 2h, and controlling the vacuum degree in the heating and heat-preservation periods within the range of 0.1-10.0 Pa. Cooling in oil at 30 deg.C for 30min, and air cooling to room temperature;
aging treatment: keeping the temperature at 710 ℃ for 8h, and keeping the vacuum degree within the range of 0.1-10.0 Pa in the temperature rising and keeping process; cooling to 610 ℃ in 1.5h along with the furnace, and preserving heat for 9 h; cooling in 43 deg.C oil for 25min, and air cooling to room temperature.
(5) And (4) separating the blank subjected to the post-processing in the step (4) from the substrate by wire cutting.
(6) And (4) machining the blank processed in the step (4) on a 3-axis machine tool, performing three-dimensional finish machining and forming, and then performing liquid sand blasting treatment to finally form the elbow part.
(6) And carrying out structure observation and mechanical property test on the metallurgical phase and the tensile sample along with the furnace.
Example 4
Example 4 provides a method for preparing a nickel-based alloy part, and with reference to example 3, example 4 differs from example 3 in that:
in the step 4, the process of the solution treatment comprises the following steps: heating to 505 ℃ along with the furnace at the speed of 10 ℃/min, preserving heat for 30min, continuously heating to 815 ℃, heating at the speed of 7 ℃/min, preserving heat for 40min, simultaneously continuously heating to 1105 ℃, heating at the speed of 5 ℃/min, preserving heat for 1.5 h;
aging treatment: 725 ℃, keeping the temperature for 9 hours, and keeping the vacuum degree within the range of 0.1 Pa-10.0 Pa in the temperature rising and keeping process; cooling to 615 ℃ along with the furnace within 1.5h, and preserving heat for 6.5 h; cooling in 45 deg.C oil for 25min, and air cooling to room temperature.
Example 5
Example 5 provides a method for preparing a nickel-based alloy part, and by taking example 3 as a reference, the difference between example 5 and example 3 is as follows:
in the step 4, the process of the solution treatment comprises the following steps: heating to 495 ℃ along with the furnace at the speed of 9 ℃/min, preserving heat for 35min, continuously heating to 825 ℃, heating at the speed of 5 ℃/min, preserving heat for 35min, simultaneously continuously heating to 1095 ℃, heating at the speed of 6 ℃/min, and preserving heat for 1.8 h;
aging treatment: preserving heat for 7 hours at 715 ℃, and keeping the vacuum degree within the range of 0.1-10.0 Pa in the temperature rising and preserving process; cooling to 628 ℃ with the furnace within 1.5h, and keeping the temperature for 7.5 h; cooling in oil at 43 deg.C for 25min, and cooling to room temperature.
Comparative example 1
Comparative example 1 provides a method for preparing a nickel-based alloy piece, and with reference to example 1, the comparative example 1 is different from example 1 in that: heating to 800 ℃ in the first aging treatment, and keeping the temperature for 15h, and cooling to 650 ℃ in the furnace within 2h in the second aging treatment, and keeping the temperature for 8 h; the procedure of example 1 was repeated except that the mixture was cooled in oil at 35 to 45 ℃ for 30 minutes and then cooled in air to room temperature.
Comparative example 2
Comparative example 2 provides a preparation method of a nickel-based alloy part, taking example 1 as a reference, and the difference between the comparative example 2 and the example 1 is that in the first aging treatment, the temperature is heated to 800 ℃ and is kept for 15h, and in the second aging treatment, the furnace is cooled to 580 ℃ within 2h and is kept for 8 h; oil cooling at 35-45 deg.C for 30min to 150 deg.C, and air cooling to room temperature, the same as example 1.
Comparative example 3
Comparative example 3 provides a preparation method of a nickel-based alloy part, taking example 1 as a reference, and the difference between the comparative example 3 and the example 1 is that in the first aging treatment, the temperature is heated to 750 ℃ and is kept for 7h, and in the second aging treatment, the furnace is cooled to 600 ℃ within 2h and is kept for 7 h; 1Bar argon + without blower cooling to below 80, and discharging, the rest is the same as the embodiment 1.
TABLE 1
As can be seen from the contents in Table 1, the tensile strength of the prepared nickel-based alloy is 1450-1489MPa, the yield strength of the prepared nickel-based alloy is 1327-1360MPa, the elongation of the prepared nickel-based alloy is 18.8-20.5 percent, and the impact energy of the prepared nickel-based alloy is 63-67J under the normal temperature condition; at the temperature of 650 ℃, the tensile strength is 1120-1130MPa, the yield strength is 960-978MPa, and the elongation is 14.9-16.2%; the nickel-based alloy prepared by the method of the comparative examples 1 to 2 has the tensile strength of 1270-1305MPa, the yield strength of 1108-1120MPa, the elongation of 132 to 13.7 percent and the impact energy of 43 to 51J under the normal temperature condition; at the temperature of 650 ℃, the tensile strength is 997-1023MPa, the yield strength is 870-878MPa, and the elongation is 12.2-13.7%; the nickel-based alloy prepared by the method provided by the comparative example 3 has the tensile strength of 1350MPa, the yield strength of 1175MPa, the elongation of 15.3 percent and the impact energy of 51J at normal temperature; at a temperature of 650 ℃, the tensile strength is 1072MPa, the yield strength is 903MPa, the elongation is 14.2%, and the yield strength and the tensile strength are inferior to those of the examples 1 to 5 of the present invention.
FIGS. 2-3 illustrate: fig. 2 and 3 are schematic diagrams of internal structures of 3D printed GH4169 alloy pieces of examples 2 and 3 after solid solution and double aging treatment, respectively, after heat treatment, incomplete recrystallization of crystal grains occurs, the crystal grains are fine and uniform, Laves phases and component segregation completely disappear, granular substances are precipitated at the crystal grain boundaries and inside the crystal grains, after two aging treatments, a fine needle-like δ phase is precipitated at the crystal grain boundaries in the first stage, a nano-scale γ "phase and a γ' phase are precipitated inside the crystal grains in the second stage, and after solid solution and double aging treatment, the number, size and distribution of precipitated phases inside the GH4169 alloy material are accurately regulated and controlled, and the existence of the phases has significant effects on the tensile strength, plasticity and high-temperature creep resistance of the material.
The invention provides a preparation method of a nickel-based alloy piece, which is characterized in that Fe and Cr are dissolved in a nickel-based matrix in a solid solution manner, so that the strength of the alloy piece is improved, element segregation can be reduced, and the tissue uniformity of the nickel-based alloy piece is improved; through the aging treatment and the control of the technological parameters in the aging treatment process, the precipitation of precipitates can be induced, so that the grain boundary strength is improved, and the high-temperature strength and the high-temperature toughness of the material are improved. By adopting the method provided by the invention, the tensile strength of the nickel-based alloy piece is 1450-1489MPa, the yield strength is 1327-1360MPa, the elongation is 18.8-20.5 percent, and the impact energy is 63-67J under the normal temperature condition; at the temperature of 650 ℃, the tensile strength is 1120-1130MPa, the yield strength is 960-978MPa, the elongation is 14.9-16.2%, the strength is high, the toughness is good, and no cracking risk exists.
While the preferred embodiments of the present application have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all alterations and modifications as fall within the scope of the application.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present application without departing from the spirit and scope of the application. Thus, if such modifications and variations of the present application fall within the scope of the claims of the present application and their equivalents, the present application is intended to include such modifications and variations as well.
Claims (10)
1. A method of making a nickel-base alloy part, comprising:
obtaining a 3D printing alloy piece;
carrying out solid solution treatment on the 3D printed alloy piece to obtain a solid solution alloy piece;
heating the solid solution alloy piece, and carrying out first time effect treatment, wherein in the first time effect treatment, the heating temperature is less than or equal to 730 ℃, and the heating time is more than or equal to 7 h;
and carrying out first cooling, heat preservation and second cooling on the first time effect alloy piece to carry out second time effect treatment to obtain the nickel-based alloy piece, wherein in the second time effect treatment, the first cooling finishing temperature is 605-.
2. The method as claimed in claim 1, wherein the first time-effect treatment comprises a heating temperature of 710-730 ℃ and a holding time of 7-10 h.
3. A method for producing a nickel-base alloy piece according to claim 1, characterized in that the second cooling end temperature during the second ageing is 20-80 ℃.
4. The method as claimed in claim 1, wherein the solution treatment of the 3D printed alloy piece comprises heating the 3D printed alloy piece to 1100 ± 10 ℃ in three stages, and keeping the temperature for 1-2h, and cooling at a rate of 130 ℃ per second and 160 ℃ per second.
5. The method according to claim 4, wherein the degree of vacuum during the solution treatment is 0.1 to 10 Pa.
6. A method for producing a nickel-base alloy piece according to claim 4, characterized in that the end-of-cooling temperature during the solution treatment is 20-80 ℃.
7. The method as claimed in claim 4, wherein the three-stage heating comprises a first heating, a second heating and a third heating, wherein in the first heating, the heating temperature is 490-510 ℃, the holding time is 30-40min, and the heating rate is 7-10 ℃/min; in the second heating, the heating temperature is 810-; in the third heating, the heating temperature is 1090-1110 ℃, the heat preservation time is 1-2h, and the heating rate is 5-8 ℃/min.
8. The method for preparing a nickel-based alloy part according to claim 4, wherein the cooling in the solution treatment is oil cooling, the temperature of oil used for oil cooling is 20-80 ℃, and the cooling time is 20-30 min.
9. The method of claim 1, wherein the obtaining of the 3D printed alloy piece comprises:
obtaining a printing program of the alloy piece;
3D laser printing is carried out on the alloy powder according to the printing program to obtain a blank piece; the alloy powder is any one of the following: GH4169 powder, GH4099 powder; the particle size of the alloy powder is 30-55 microns, in the 3D laser printing process, the laser power is 200-400W, the scanning speed is 800-1200 mm/s, the powder spreading layer thickness is 40-60 microns, the laser lapping interval is 0.6-1.2 mm, the light spot compensation is 0.07-0.12 mm, and the substrate thickness is 35-45 mm;
and performing powder cleaning treatment on the blank piece to obtain a 3D printing alloy piece.
10. A nickel-base alloy piece, characterized in that it has been produced by the method for producing a nickel-base alloy piece according to any of claims 1 to 9.
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| CN114643368A (en) * | 2022-02-28 | 2022-06-21 | 西安航天发动机有限公司 | Heat treatment method for additive manufacturing high-temperature alloy working in oxygen-enriched high-temperature environment |
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| CN112828310A (en) * | 2020-12-31 | 2021-05-25 | 湖北三江航天红阳机电有限公司 | Method for improving toughness of 3D printing nickel-based high-temperature alloy part |
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