CN114480893B - Method for reducing additive manufacturing cracks of nickel-based superalloy and nickel-based superalloy - Google Patents
Method for reducing additive manufacturing cracks of nickel-based superalloy and nickel-based superalloy Download PDFInfo
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- CN114480893B CN114480893B CN202111671837.5A CN202111671837A CN114480893B CN 114480893 B CN114480893 B CN 114480893B CN 202111671837 A CN202111671837 A CN 202111671837A CN 114480893 B CN114480893 B CN 114480893B
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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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/023—Alloys based on nickel
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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
- 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
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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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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- 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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Abstract
The invention discloses a method for reducing additive manufacturing cracks of a nickel-based superalloy and the nickel-based superalloy, wherein the method comprises the steps of taking nickel-based superalloy powder as a raw material, mixing Re powder, and forming by an additive manufacturing technology; wherein the Re powder exists in a content of 0.5-2.0% by mass. The rare earth element Re is added, so that dendritic crystal grains of the nickel-based high-temperature alloy after heat treatment are finer, a gamma' phase in the nickel-based alloy is precipitated and precipitated, a matrix is strengthened, and the mechanical property of the alloy in a high-temperature state is greatly improved, so that the nickel-based high-temperature alloy is widely applied to severe places with high temperature such as turbine engines and the like.
Description
Technical Field
The invention belongs to the technical field of organic compound synthesis, and particularly relates to a method for reducing additive manufacturing cracks of a nickel-based superalloy and the nickel-based superalloy.
Background
In recent years, with the gradual development of 3D printing technology, the selective laser melting technology is more and more applied to the printing of metal parts, the rapid manufacturing of nickel-based high-temperature alloy parts makes a great breakthrough, and particularly, the direct manufacturing of the nickel-based high-temperature alloy parts is performed through the selective laser melting technology (SLM), so that the manufacturing efficiency and the optimized upgrading of important parts in the fields of aerospace, petrochemical industry and the like are greatly promoted. The laser additive manufacturing technology can meet the requirement of manufacturing parts with complex structures, high precision and high strength, and has great market potential. However, in the laser additive manufacturing process, the repeated rapid heating and rapid cooling can generate great welding stress in the cladding layer and the base material, so that various welding cracks are induced, the quality of the cladding layer is not up to the standard and the cladding layer cannot be used, the printed finished piece has high residual stress, the printed piece is easy to deform and crack, the influence on the performance of the printed piece is large, and the production and application of the laser additive manufacturing technology are greatly limited.
Disclosure of Invention
This section is for the purpose of summarizing some aspects of embodiments of the invention and to briefly introduce some preferred embodiments. In this section, as well as in the abstract and the title of the invention of this application, simplifications or omissions may be made to avoid obscuring the purpose of the section, the abstract and the title, and such simplifications or omissions are not intended to limit the scope of the invention.
The present invention has been made keeping in mind the above and/or other problems occurring in the prior art.
One of the purposes of the invention is to provide a method for improving the mechanical property of a nickel-based high-temperature alloy, which is provided by the invention, by adding a proper content of Re element into the nickel-based high-temperature alloy for micro-alloying, a rhenium effect is generated, the coarsening degree of a gamma' phase is reduced, the increase of a harmful phase Laves phase and carbide is inhibited, the compactness of the material is improved, and the improvement of the mechanical property of the material is facilitated.
In order to solve the technical problems, the invention provides the following technical scheme: a method for reducing the additive manufacturing cracks of nickel-based superalloy comprises the steps of taking nickel-based superalloy powder as a raw material, mixing Re powder, and forming by an additive manufacturing technology;
wherein the Re powder exists in a mass fraction of 0.5-2.0%.
As a preferable scheme of the method for reducing the cracks of the nickel-base superalloy in the additive manufacturing process, the method comprises the following steps: the nickel-based high-temperature alloy powder comprises, by mass, 17-21% of Cr, 10-15% of Fe, 2.8-3.3% of Mo, 4.75-5.50% of Nb, 14-23% of Co, 0.01-0.08% of C, 0.01-0.35% of Mn, 0.15-0.35% of Si, 0.01-0.30% of Cu, 0.20-0.80% of Al, 0.65-1.15% of Ti, 0.001-0.006% of B and the balance of Ni.
As a preferable scheme of the method for reducing the cracks of the nickel-base superalloy in the additive manufacturing process, the method comprises the following steps: the additive manufacturing technology is one of selective laser melting, electron beam melting or coaxial powder feeding laser forming.
As a preferable scheme of the method for reducing the cracks of the nickel-base superalloy in the additive manufacturing process, the method comprises the following steps: the selective laser melting has the laser power of 100-400W, the laser scanning speed of 75-500 mm/s, the spot diameter of 50-100 microns, the laser scanning interval of 40-110 microns, the powder layer thickness of 30-50 microns and the laser scanning direction rotation of 45-90 degrees between the forming layers.
As a preferable scheme of the method for reducing the additive manufacturing cracks of the nickel-based superalloy, the method comprises the following steps: further comprises heat treatment after the additive manufacturing technology is formed;
the heat treatment is solid solution at 1100 ℃ for 1h, aging at 720 ℃ for 8h, cooling to 620 ℃ at the rate of 100 ℃/h, aging for 10h, and finally cooling in water.
Another object of the present invention is to provide a nickel-based superalloy powder for 3D printing, including a nickel-based superalloy powder and Re powder, the Re powder being present in an amount of 0.5 to 2.0% by mass.
As a preferable aspect of the nickel-based superalloy powder for 3D printing of the present invention, wherein: the nickel-based high-temperature alloy powder comprises, by mass, 17-21% of Cr, 10-15% of Fe, 2.8-3.3% of Mo, 4.75-5.50% of Nb, 14-23% of Co, 0.01-0.08% of C, 0.01-0.35% of Mn, 0.15-0.35% of Si, 0.01-0.30% of Cu, 0.20-0.80% of Al, 0.65-1.15% of Ti, 0.001-0.006% of B and the balance of Ni.
As a preferable aspect of the nickel-based superalloy powder for 3D printing of the present invention, wherein: the oxygen content of the nickel-based superalloy powder is less than or equal to 0.02wt%, and the sulfur content is less than or equal to 0.008wt%.
As a preferable aspect of the nickel-based superalloy powder for 3D printing of the present invention, wherein: the average size of the nickel-based superalloy powder is 23-47 mu m; the average size of Re powder is 8-32 μm.
Another object of the present invention is to provide a nickel-base superalloy, which is formed by additive manufacturing technology using the nickel-base superalloy powder for 3D printing as described in any of the above.
Compared with the prior art, the invention has the following beneficial effects:
the rare element Re is added, so that dendritic crystal grains of the nickel-based high-temperature alloy after heat treatment are finer, the gamma' phase in the nickel-based alloy is precipitated and precipitated, a matrix is strengthened, and the mechanical property of the alloy in a high-temperature state is greatly improved, so that the nickel-based high-temperature alloy is widely applied to severe high-temperature places such as turbine engines and the like.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the description of the embodiments will be briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without inventive exercise. Wherein:
FIG. 1 is a histogram of the structure of a nickel-base superalloy specimen prepared in example 1 of the present invention.
Fig. 2 is a surface microscopic view of the nickel-based superalloy specimens prepared in comparative example 1.
Fig. 3 is a surface microscopic view of the nickel-base superalloy specimens prepared in comparative example 2.
Detailed Description
In order to make the aforementioned objects, features and advantages of the present invention more comprehensible, specific embodiments thereof are described in detail below with reference to examples of the specification.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, however, the present invention may be practiced otherwise than as specifically described herein, and it will be appreciated by those skilled in the art that the present invention may be practiced without departing from the spirit and scope of the present invention and that the present invention is not limited by the specific embodiments disclosed below.
Furthermore, reference herein to "one embodiment" or "an embodiment" means that a particular feature, structure, or characteristic described in connection with the embodiment is included in at least one implementation of the invention. The appearances of the phrase "in one embodiment" in various places in the specification are not necessarily all referring to the same embodiment, nor are separate or alternative embodiments mutually exclusive of other embodiments.
Example 1
(1) IN this embodiment 1, the following IN718 nickel-based superalloy is used, to which a rare element Re is added IN an amount of 0.5 mass%, and the IN718 nickel-based superalloy has the mass percentage: 20% of Cr, 12% of Fe, 3% of Mo, 5% of Nb, 18% of Co, 0.05% of C, 0.02% of Mn, 0.2% of Si, 0.02% of Cu, 0.5% of Al, 1% of Ti, 0.005% of B and the balance of Ni.
(2) The IN718 primary particle size was sufficiently fine that to reduce the total milling time, the powder mixture was prepared IN two stages. The first stage is mechanical alloying, and the weight ratio of the IN718 nickel-base superalloy to the Re powder is 1; IN the second stage, the remaining IN718 powder was added to mix to obtain a powder mixture. Milling was carried out in a single ball mill at a constant speed of 200rpm and 25 balls with a diameter of 25 mm.
(3) Placing the mixed powder into SLM forming equipment, selecting 304 stainless steel as a substrate, preheating the substrate to 120 ℃, introducing high-purity argon with the purity of 99.99wt.% to enable the oxygen content to be less than or equal to 450ppm, and carrying out SLM forming, wherein selective laser melting forming parameters are as follows: the laser power was 400W, the laser scanning rate was 500mm/s, the powder layer thickness was 50 μm, and the laser scanning direction between the shaping layers was rotated 67 °.
(4) And after 3D printing is finished, carrying out heat treatment, carrying out solid solution at 1100 ℃ for 1h, carrying out aging at 720 ℃ for 8h, cooling to 620 ℃ at the speed of 100 ℃/h, carrying out aging for 10h, and finally cooling in water to obtain the nickel-based high-temperature alloy sample.
The columnar crystal diagram in the nickel-based superalloy sample structure is shown in figure 1, and as can be seen from figure 1, the printed piece structure is uniform, the growth direction of the columnar crystal is basically the same as the cooling direction of the temperature of a molten pool, the crystal grains are refined, the growth of cracks is inhibited, and the mechanical property is improved.
The physical property test of the obtained nickel-based high-temperature alloy sample shows that the density reaches 99 percent, the tensile strength is 1050Mpa, and the performance is excellent.
Comparative example 1
(1) The comparative example 1 adopts the following IN718 nickel-based superalloy without adding rare element Re, and the IN718 nickel-based superalloy has the following mass percentage: 20% of Cr, 12% of Fe, 3% of Mo, 5% of Nb, 18% of Co, 0.05% of C, 0.02% of Mn, 0.2% of Si, 0.02% of Cu, 0.5% of Al, 1% of Ti, 0.005% of B and the balance of Ni.
(2) To control experimental variables, the alloy powder was also ball milled. Milling was carried out in a single ball mill at a constant speed of 200rpm and 25 balls with a diameter of 25 mm.
(3) Putting the mixed powder into SLM forming equipment, selecting 304 stainless steel as a substrate, preheating the substrate to 120 ℃, introducing high-purity argon with the purity of 99.99wt.%, enabling the oxygen content to be less than or equal to 450ppm, and carrying out SLM forming, wherein selective laser melting forming parameters are as follows: the laser power was 400W, the laser scanning rate was 500mm/s, the powder layer thickness was 50 μm, and the laser scanning direction between the shaping layers was rotated 67 °.
(4) And after 3D printing is finished, carrying out heat treatment, carrying out solid solution at 1100 ℃ for 1h, carrying out aging at 720 ℃ for 8h, cooling to 620 ℃ at the speed of 100 ℃/h, carrying out aging for 10h, and finally cooling in water to obtain the nickel-based high-temperature alloy sample.
The microstructure surface microscopic image of the nickel-based superalloy sample is shown in FIG. 2, and a printed piece has microcracks.
The physical property test of the obtained nickel-based superalloy sample shows that the tensile strength is 720MPa.
Comparative example 2
(1) The following IN718 nickel-based superalloy is adopted IN the comparative example 2, rare element Re is added IN an amount of 1.5% by mass, and the mass percentage of the IN718 nickel-based superalloy is as follows: 20% of Cr, 12% of Fe, 3% of Mo, 5% of Nb, 18% of Co, 0.05% of C, 0.02% of Mn, 0.2% of Si, 0.02% of Cu, 0.5% of Al, 1% of Ti, 0.005% of B and the balance of Ni.
(2) The powder mixture was prepared in two stages. The first is mechanical alloying, the weight ratio of the IN718 nickel-base superalloy to the Re powder is 1; IN the second stage, a powder mixture was obtained by adding the right amount of pure IN718 powder. Milling was carried out in a single ball mill at a constant speed of 200rpm and 25 balls with a diameter of 25 mm.
(3) Putting the mixed powder into SLM forming equipment, selecting 304 stainless steel as a substrate, preheating the substrate to 120 ℃, introducing high-purity argon with the purity of 99.99wt.%, enabling the oxygen content to be less than or equal to 450ppm, and carrying out SLM forming, wherein selective laser melting forming parameters are as follows: the laser power was 400W, the laser scanning rate was 500mm/s, the powder layer thickness was 50 μm, and the laser scanning direction between the shaping layers was rotated 67 °.
(4) And after 3D printing is finished, carrying out heat treatment, carrying out solid solution at 1100 ℃ for 1h, carrying out aging at 720 ℃ for 8h, cooling to 620 ℃ at the speed of 100 ℃/h, carrying out aging for 10h, and finally cooling in water to obtain the nickel-based high-temperature alloy sample.
The microscopic picture of the surface of the nickel-based superalloy sample is shown in fig. 3, and a printed piece has more microcracks.
The physical property test of the obtained nickel-based superalloy sample shows that the tensile strength is 648MPa.
The invention provides a method for adding Re with proper content to perform rare microalloying to generate a rhenium effect, so that the coarsening degree of a gamma' phase is reduced, the increase of a harmful phase Laves phase and carbide is inhibited, dendritic crystal grains of an IN718 part after heat treatment are finer, the density of the material is improved, and the improvement of the mechanical property of the material is facilitated. The IN718 nickel-based superalloy prepared by the method has the advantages that the number of cracks is obviously reduced, the sample part is mostly IN equiaxial columnar crystal structure, and the tensile strength reaches 1050MPa.
It should be noted that the above-mentioned embodiments are only for illustrating the technical solutions of the present invention and not for limiting, and although the present invention has been described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, which should be covered by the claims of the present invention.
Claims (8)
1. A method for reducing additive manufacturing cracks of a nickel-based superalloy is characterized by comprising the following steps: comprises the steps of (a) preparing a mixture of a plurality of raw materials,
adding Re powder with the mass percent of 0.5% into nickel-based superalloy powder serving as a raw material, and forming by an additive manufacturing technology;
the nickel-based superalloy powder comprises, by mass, 20% of Cr, 12% of Fe, 3% of Mo, 5% of Nb, 18% of Co, 0.05% of C, 0.02% of Mn, 0.2% of Si, 0.02% of Cu, 0.5% of Al, 1% of Ti, 0.005% of B and the balance of Ni.
2. The method of reducing nickel-base superalloy additive manufacturing cracks of claim 1, wherein: the additive manufacturing technology is one of selective laser melting, electron beam melting or coaxial powder feeding laser forming.
3. The method of reducing nickel-base superalloy additive manufacturing cracks of claim 2, wherein: the selective laser melting is carried out, the laser power is 100-400W, the laser scanning speed is 75-500 mm/s, the diameter of a light spot is 50-100 mu m, the laser scanning interval is 40-110 mu m, the powder spreading layer thickness is 30-50 mu m, and the laser scanning direction between forming layers is rotated by 45-90 degrees.
4. The method for reducing the cracks of the nickel-base superalloy as in any of claims 1 to 3, wherein: further comprises heat treatment after the additive manufacturing technology is formed;
the heat treatment is solid solution at 1100 ℃ for 1h, aging at 720 ℃ for 8h, cooling to 620 ℃ at the rate of 100 ℃/h, aging for 10h, and finally cooling in water.
5. A nickel-based superalloy powder for 3D printing, comprising: the alloy comprises nickel-based superalloy powder and Re powder, wherein the Re powder is present in a mass fraction of 0.5%;
the nickel-based superalloy powder comprises, by mass, 20% of Cr, 12% of Fe, 3% of Mo, 5% of Nb, 18% of Co, 0.05% of C, 0.02% of Mn, 0.2% of Si, 0.02% of Cu, 0.5% of Al, 1% of Ti, 0.005% of B and the balance of Ni.
6. Nickel-base-superalloy powder for 3D printing according to claim 5, wherein: the oxygen content of the nickel-based superalloy powder is less than or equal to 0.02wt%, and the sulfur content is less than or equal to 0.008wt%.
7. Nickel-base-superalloy powder for 3D printing according to claim 5 or 6, wherein: the average size of the nickel-based superalloy powder is 23-47 mu m; the average size of the Re powder is 8-32 mu m.
8. A nickel-base superalloy, characterized by: the nickel-based superalloy powder for 3D printing according to any one of claims 5 to 7 is formed through an additive manufacturing technology.
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| CN114799204B (en) * | 2022-06-17 | 2022-12-27 | 暨南大学 | Method for reducing brittle Laves phase in laser additive manufacturing nickel-based high-temperature alloy and improving strong plasticity |
| CN115555555A (en) * | 2022-10-24 | 2023-01-03 | 北京工业大学 | Method for inhibiting hot cracks of high-temperature alloy manufactured by laser additive manufacturing |
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| CN109554584A (en) * | 2018-08-28 | 2019-04-02 | 中南大学 | A kind of nickel-base alloy, preparation method and manufacture article |
| CN111101022B (en) * | 2018-10-29 | 2022-03-22 | 利宝地工程有限公司 | High gamma prime nickel-based superalloy, use thereof and method of manufacturing a turbine engine component |
| DE102019213990A1 (en) * | 2019-09-13 | 2021-03-18 | Siemens Aktiengesellschaft | Nickel-based alloy for additive manufacturing, process and product |
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| CN112011713B (en) * | 2020-08-30 | 2021-11-23 | 中南大学 | Method for eliminating cracks of 3D printing nickel-based superalloy |
| CN111906311B (en) * | 2020-08-30 | 2021-05-28 | 中南大学 | Method for preventing selective laser melting nickel-based high-temperature alloy from cracking |
| CN113020598B (en) * | 2021-03-03 | 2022-03-11 | 西北工业大学 | Selective laser melting formed nickel-based high-temperature alloy and preparation method thereof |
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Effective date of registration: 20221115 Address after: Yuelu District City, Hunan province 410083 Changsha Lushan Road No. 932 Patentee after: CENTRAL SOUTH University Patentee after: AECC SOUTH INDUSTRY Co.,Ltd. Address before: 410083 Hunan province Changsha Lushan Road No. 932 Patentee before: CENTRAL SOUTH University |