CN111360266A - Selective laser melting forming Inconel718 alloy and heat treatment method thereof - Google Patents
Selective laser melting forming Inconel718 alloy and heat treatment method thereof Download PDFInfo
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- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
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- 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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- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
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- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
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- B33—ADDITIVE MANUFACTURING TECHNOLOGY
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- 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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- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
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Abstract
The invention belongs to the technical field of metal additive manufacturing and high-temperature alloy heat treatment, and particularly relates to a selective laser melting forming Inconel718 alloy and a heat treatment method thereof. The heat treatment method comprises the following process steps: 1) the formed Inconel718 specimens were hot isostatic pressed at 1080 ℃. 2) The hot isostatic pressed sample was subjected to solution heat treatment at 980 ℃. 3) And (3) performing double-aging heat treatment on the solid-dissolved sample at 720 ℃ and 620 ℃ in sequence. According to the heat treatment method, high-temperature hot isostatic pressing heat treatment is added before conventional solid solution heat treatment, the heat preservation time of solid solution and double aging heat treatment is prolonged, brittle Laves phases and micro-pores existing in an Inconel718 alloy sample formed by selective laser melting are eliminated, precipitation of strengthening phases is effectively promoted, the ductility of the material is greatly kept while the strength of the material is remarkably improved, and good comprehensive mechanical properties are obtained.
Description
Technical Field
The invention relates to the technical field of metal additive manufacturing technology and high-temperature alloy heat treatment, in particular to a selective laser melting forming Inconel718 alloy and a heat treatment method thereof.
Background
The Inconel718 alloy is an important material which can be applied to high temperature and high load, and is widely applied to the fields of aerospace, nuclear industry and energy due to good high-temperature mechanical properties and excellent high-temperature corrosion resistance and oxidation resistance.
The Inconel718 alloy mainly contains a γ "(Ni3Nb) phase as a main reinforcing phase, and γ' (Ni3(Al, Ti, Nb)) and δ (Ni3Nb) phases as auxiliary reinforcing phases. By adopting different forming modes and heat treatment processes, the Inconel718 alloy parts with different microstructures and mechanical properties can be obtained, and the application standards of different fields can be met.
The conventional Incoll 718 alloy part is mainly prepared by two modes of casting and forging.
Although the two processes are continuously developed and improved, the casting still has the problems of serious element segregation, large crystal grains, shrinkage porosity and the like; the performance of the forging is higher than that of the cast state, but the forging is difficult to form parts with complex shapes due to process limitation, and the forging has the defects of black spots, white spots and the like.
These problems not only affect the performance of the alloy, but also limit the range of applications for the Inconel718 alloy.
Currently, parts with uniform tissues, fine grains, high density and complex shapes can be formed by controlling the technological parameters (such as Laser scanning speed, power, scanning distance and the like) of Selective Laser Melting (SLM). However, due to the forming characteristics of rapid cooling and rapid solidification of the selective laser melting forming technology, the formed Inconel718 alloy part generally has the defects of large local thermal stress, precipitation of a large amount of brittle Laves phases caused by Nb element segregation, inhibition of precipitation of gamma, gamma and delta phases, easiness in generation of microcracks in a boundary remelting region of a melting channel and the like, and the defects of a formed sample can be improved to a certain extent through proper heat treatment.
At present, the post-treatment process of the Inconel718 alloy formed by selective laser melting mainly adopts a standard heat treatment scheme of a traditional cast-forged piece, the unique problem of selective laser melting cannot be effectively solved, although the strength of most of materials subjected to heat treatment is obviously enhanced, the elongation after fracture of a sample is lower than the forging standard (Q/3B548-1996), mainly because the solid solution temperature of standard heat treatment is lower, the high-melting-point Laves phase is not completely eliminated at the temperature, the material is easy to generate micro cracks under the action of external force, and the lower heat treatment temperature is not beneficial to release of Nb element, so that the quantity of precipitated strengthening phases is reduced.
Meanwhile, microscopic gaps generated in the laser forming process in the alloy cannot be eliminated, and cracks are easily formed when the material is subjected to the action of external force, so that the material fails prematurely. Therefore, certain improvement needs to be made on the existing standard heat treatment, the material performance is expected to be further improved by optimizing the heat treatment scheme of the Inconel718 alloy sample, and an important basis is provided for the application of forming the Inconel718 alloy by selective laser melting.
Disclosure of Invention
The invention provides an Inconel718 alloy formed by selective laser melting and a heat treatment method thereof. The invention aims to improve the standard heat treatment scheme of the existing Inconel718 alloy casting and forging piece, effectively improve the strength and the elongation after fracture of the alloy after heat treatment, and provide an important basis for the application of the Inconel718 alloy in selective laser melting forming.
According to the treatment method, high-temperature hot isostatic pressing heat treatment is added before conventional solid solution heat treatment, the heat preservation time of solid solution and double aging heat treatment is prolonged, brittle Laves phases and microscopic pores existing in an Inconel718 alloy sample formed by selective laser melting are eliminated, the precipitation of strengthening phases is effectively promoted, the ductility of the material is greatly kept while the strength of the material is remarkably improved, and good comprehensive mechanical properties are obtained.
The invention is realized by the following technical scheme:
a heat treatment method for performance of an Inconel718 alloy formed by selective laser melting comprises the following steps:
step (1): carrying out high-temperature hot isostatic pressing heat treatment on the Inconel718 sample melted and formed in the selected laser area, and then introducing air to rapidly cool the sample to room temperature;
step (2): carrying out solution treatment on the Inconel718 sample treated in the step (1), and then discharging from the furnace and air-cooling to room temperature;
and (3): and (3) carrying out double-aging heat treatment on the sample treated in the step (2), and then discharging and air-cooling to room temperature.
In the hot isostatic pressing heat treatment process in the step (1), the hot isostatic pressing heat treatment temperature is 1050-1120 ℃, the pressure is 1400-1480 bar, and the heat preservation time is 90-120 min; the preferable technological parameters are as follows: the temperature is 1080 ℃, the pressure is 1480bar, and the heat preservation time is 120 min.
In the process of the solid solution treatment in the step (2), the temperature of the solid solution treatment is 940-980 ℃, and the heat preservation time is 80-120 min; the preferable technological parameters are as follows: the temperature is 980 ℃ and the heat preservation time is 90 min.
In the aging heat treatment process in the step (3), the temperature of the aging heat treatment is 700-720 ℃, the heat preservation time is 480-540 min, the furnace is cooled to 600-620 ℃ at 48-55 ℃/h, and then the heat preservation is continued for 480-540 min; the preferable technological parameters are as follows: the temperature is 720 ℃, the heat preservation time is 480min, the furnace is cooled to 620 ℃ at the speed of 50 ℃/h, and the heat preservation is continued for 540 min.
The heating speed of the hot isostatic pressing thermal equipment in the step (1) is 7-8 ℃/min, and the pressure increasing speed is 10-11 bar/min; the preferable technological parameters are as follows: the temperature rise rate is 8 ℃/min, and the pressure rise rate is 11 bar/min.
In the heat treatment process in the step (2) and the step (3), the temperature rise speed of the furnace is the same, namely 5-6 ℃/min; preferably 6 deg.C/min.
Compared with the prior art, the invention has the following advantages and effects:
hot isostatic pressing heat treatment is carried out in the step (1), the heat treatment temperature is 1080 ℃, the pressure is 1480bar, heat preservation is carried out for 120min, and then air is introduced to rapidly cool to the room temperature; aims to eliminate the internal micro-pores of the sample by high pressure and dissolve the brittle Laves phase by high temperature, thereby reducing element segregation, homogenizing the structure and promoting the recrystallization of crystal grains.
Carrying out solution treatment in the step (2), wherein the heat treatment temperature is 980 ℃, the heat preservation time is 90min, and then discharging from the furnace and air cooling to room temperature; the purpose is to promote the separation of delta phase, regulate and control the distribution, the form and the size of the delta phase and reduce the notch sensitivity of the material.
The double aging heat treatment in the step (3) of the invention comprises the steps of firstly raising the temperature of a sample to 720 ℃, preserving the heat for 480min, continuously preserving the heat for 540min after furnace cooling to 620 ℃ at a speed of 50 ℃/h, and then discharging and air cooling to room temperature; the aim is to obtain a gamma 'phase and a gamma' phase which are fine and evenly distributed, and a reinforced material.
In conclusion, the high-temperature hot isostatic pressing heat treatment is added before the conventional heat treatment, the heat preservation time of the solid solution and double aging heat treatment is prolonged, the brittle Laves phase and the internal microscopic pores of the alloy in the Inconel718 alloy sample formed by selective laser melting are eliminated, and the precipitation of the strengthening phase is effectively promoted; compared with a sample before heat treatment, the tensile strength at room temperature is improved by 37.06%, the yield strength at room temperature is improved by 70.14%, the hardness at room temperature is improved by 61.18%, and the elongation after fracture is higher than the standard of a forging piece (12.00%) and reaches 13.30%;
the ductility of the material is greatly maintained while the room temperature strength of the material is remarkably improved, and the good comprehensive mechanical property is obtained, so that the method has great significance for widening the application range of the Inconel718 alloy.
Drawings
FIG. 1 is a 2000-fold magnified microstructure of a sample of the present invention prior to heat treatment.
FIG. 2 is a 2000-fold magnified microstructure of a sample of the present invention after treatment in step (1).
FIG. 3 is a 2000-fold magnified microstructure of a sample of the present invention after heat treatment in steps (1), (2), and (3).
FIG. 4 is a graph of the heat treatment process of the present invention and a standard heat treatment process.
Detailed Description
The present invention will be described in further detail with reference to specific examples.
Example 1
The invention discloses a heat treatment method for improving the performance of an Inconel718 alloy formed by selective laser melting, which can be realized by the following process steps:
step (1): carrying out high-temperature hot isostatic pressing heat treatment on the Inconel718 sample melted and formed in the selected laser area, and then introducing air to rapidly cool the sample to room temperature;
the specific technological parameters of the step are as follows: the hot isostatic pressing heat treatment temperature is 1050-1120 ℃, the pressure is 1400-1480 bar, and the heat preservation time is 90-120 min;
the technological parameters of the embodiment are as follows: the temperature is 1080 ℃, the pressure is 1480bar, and the heat preservation time is 120 min.
Wherein the heating rate of the hot isostatic pressing thermal equipment is 7-8 ℃/min, and the pressure rise rate is 10-11 bar/min; the preferable technological parameters are as follows: the temperature rise rate is 8 ℃/min, and the pressure rise rate is 11 bar/min.
Step (2): carrying out solution treatment on the Inconel718 sample treated in the step (1), and then discharging from the furnace and air-cooling to room temperature;
the specific technological parameters of the step are as follows: the temperature of the solution treatment is 940-980 ℃, and the heat preservation time is 80-120 min;
the technological parameters of the embodiment are as follows: the temperature is 980 ℃ and the heat preservation time is 90 min.
And (3): carrying out double-aging heat treatment on the sample treated in the step (2), and then discharging and air-cooling to room temperature;
the specific technological parameters of the step are as follows: the temperature of the aging heat treatment is 700-720 ℃, the heat preservation time is 480-540 min, the furnace is cooled to 600-620 ℃ at 48-55 ℃/h, and then the heat preservation is continued for 480-540 min;
the preferred process parameters of the embodiment are as follows: the temperature is 720 ℃, the heat preservation time is 480min, the furnace is cooled to 620 ℃ at the speed of 50 ℃/h, and the heat preservation is continued for 540 min.
Example 2
This embodiment has the same features as embodiment 1 except for the following features.
In the heat treatment process in the step (2) and the step (3), the temperature rise speed of the furnace is the same, namely 5-6 ℃/min; both are preferably 6 deg.C/min.
The Inconel718 alloy obtained in the above embodiment of the present invention and the performance improvement thereof will be further described with reference to fig. 1 to 3.
FIG. 1 is a 2000-fold magnified microstructure of a sample of the present invention prior to heat treatment.
FIG. 1 shows the structure of a sample after being polished and corroded by a corrosive liquid, which is observed by a scanning electron microscope. It can be seen that the alloy has obvious overlap joint boundary before heat treatment, and a large amount of dendritic structures exist in the arc-shaped molten pool and on the overlap joint boundary, and white precipitates among dendritic crystals are brittle Laves phases.
The density of the sample at this time was 99.27% as measured by archimedes drainage method. The mechanical properties of the alloy are tested by a micro Vickers hardness tester and an electronic universal tester, and the alloy is tested to obtain the alloy with the room-temperature hardness of 304HV0.2, the room-temperature tensile strength of 993MPa, the room-temperature yield strength of 700MPa and the room-temperature elongation at break of 20.37%.
FIG. 2 is a 2000-fold magnified microstructure of a sample after treatment in step (1).
FIG. 2 shows the structure of the sample after polishing and chemical etching by scanning electron microscope. It can be seen that after the step (1), the lap joint boundary in fig. 1 disappears, the dendrite substructure also basically disappears, meanwhile, a large amount of brittle Laves phases precipitated among the dendrites are basically dissolved, only a small amount of precipitated phases remain in the grain boundary, and at this time, the grain boundary is straightened, which indicates that the recrystallization is basically completed and the Nb element is homogenized.
The density of the sample at the moment is measured by adopting an Archimedes drainage method99.84 percent. The mechanical property is tested by adopting a micro Vickers hardness tester and an electronic universal tester, and the room temperature hardness is 266HV0.2。
FIG. 3 is a 2000-fold magnified microstructure of a sample after heat treatment in steps (1), (2), and (3).
FIG. 3 shows the microstructure of the sample after polishing and chemical corrosion observed by scanning electron microscope, wherein short rod-like and granular delta phases are distributed at the grain boundary and inside the grain.
The precipitated phase is analyzed by X-ray diffraction, a delta phase, a gamma 'phase and a gamma' phase are detected, the mechanical properties are tested by a micro Vickers hardness tester and an electronic universal tester, and the room-temperature hardness is 490HV0.2, the room-temperature tensile strength is 1361MPa, the room-temperature yield strength is 1191MPa, and the room-temperature elongation after fracture is 13.30%.
In conclusion, the Inconel718 alloy sample subjected to the heat treatment process basically eliminates internal microscopic pores and element segregation, grains are obviously refined, a second phase is uniformly precipitated, the room-temperature tensile strength reaches 1361MPa, the room-temperature yield strength reaches 1191MPa, the elongation after fracture reaches 13.30%, and the tensile strength and the element segregation are all higher than the standard of forgings. Can meet the requirements of high strength and high plasticity of the Inconel718 alloy structural member.
As described above, the present invention can be preferably realized.
The embodiments of the present invention are not limited to the above-described embodiments, and any other changes, modifications, substitutions, combinations, and simplifications which do not depart from the spirit and principle of the present invention should be construed as equivalents thereof, and they are included in the scope of the present invention.
Claims (8)
1. A heat treatment method for forming Inconel718 alloy performance through selective laser melting is characterized in that the heat treatment combines high-temperature hot isostatic pressing, solid solution and double aging, and specifically comprises the following steps:
step (1): carrying out high-temperature hot isostatic pressing heat treatment on the Inconel718 sample melted and formed in the selected laser area, and then introducing air to rapidly cool the sample to room temperature;
step (2): carrying out solution treatment on the Inconel718 sample treated in the step (1), and then discharging from the furnace and air-cooling to room temperature;
and (3): and (3) carrying out double-aging heat treatment on the sample treated in the step (2), and then discharging and air-cooling to room temperature.
2. The heat treatment method for improving the performance of the Inconel718 alloy formed by selective laser melting according to claim 1, wherein the hot isostatic pressing heat treatment in the step (1) is performed at 1050-1120 ℃, 1400-1480 bar and 90-120 min.
3. The heat treatment method for improving the performance of the Inconel718 alloy formed by selective laser melting according to claim 2, wherein the solution treatment temperature in the step (2) is 940-980 ℃, and the heat preservation time is 80-120 min.
4. The heat treatment method for improving the performance of the Inconel718 alloy formed by selective laser melting according to claim 3, wherein in the step (3), the aging heat treatment temperature is 700-720 ℃, the heat preservation time is 480-540 min, and after the temperature is reduced to 600-620 ℃ by a furnace at a rate of 48-55 ℃/h, the heat preservation is continued for 480-540 min.
5. The heat treatment method for improving the performance of the Inconel718 alloy formed by selective laser melting according to claim 4, wherein the heating rate of the hot isostatic pressing thermal equipment in the step (1) is 7-8 ℃/min, and the pressure rise rate is 10-11 bar/min.
6. The heat treatment method for improving the performance of the Inconel718 alloy formed by selective laser melting according to claim 1, wherein the temperature rise speed of the heat treatment furnace in the step (2) is 5-6 ℃/min.
7. The heat treatment method for improving the performance of the Inconel718 alloy formed by selective laser melting according to claim 1, wherein the temperature rise speed of the heat treatment furnace in the step (3) is 5-6 ℃/min.
8. An Inconel718 alloy, characterized by being obtained by the heat treatment method of any one of claims 1 to 7.
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| CN114752873A (en) * | 2022-03-16 | 2022-07-15 | 上海大学 | Heat treatment method of ultrahigh-plasticity Inconel718 alloy prepared based on SLM |
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