CN115502416B - Laser selective melting forming GH4099 high-temperature alloy heat treatment method - Google Patents
Laser selective melting forming GH4099 high-temperature alloy heat treatment method Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 51
- 239000000956 alloy Substances 0.000 title claims abstract description 51
- 238000010438 heat treatment Methods 0.000 title claims abstract description 41
- 238000002844 melting Methods 0.000 title claims abstract description 30
- 230000008018 melting Effects 0.000 title claims abstract description 30
- 238000000034 method Methods 0.000 title claims abstract description 30
- 229910000601 superalloy Inorganic materials 0.000 claims abstract description 64
- 238000001513 hot isostatic pressing Methods 0.000 claims abstract description 56
- 230000032683 aging Effects 0.000 claims abstract description 27
- 230000007547 defect Effects 0.000 claims abstract description 10
- 238000004857 zone melting Methods 0.000 claims abstract description 9
- 239000000243 solution Substances 0.000 claims description 40
- 238000004321 preservation Methods 0.000 claims description 32
- 239000006104 solid solution Substances 0.000 claims description 31
- 238000001816 cooling Methods 0.000 claims description 28
- 238000005728 strengthening Methods 0.000 claims description 10
- 210000003850 cellular structure Anatomy 0.000 claims description 9
- 239000011159 matrix material Substances 0.000 claims description 6
- 239000013078 crystal Substances 0.000 claims description 5
- 230000008569 process Effects 0.000 claims description 5
- 238000004590 computer program Methods 0.000 description 7
- 238000010586 diagram Methods 0.000 description 7
- 238000012545 processing Methods 0.000 description 5
- 230000006870 function Effects 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000000462 isostatic pressing Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 238000003860 storage Methods 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000009694 cold isostatic pressing Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000007596 consolidation process Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000011534 incubation Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
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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
- 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
- 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
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
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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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- 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
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- 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 application discloses a heat treatment method for forming GH4099 high-temperature alloy by selective laser melting, which comprises the following steps: setting hot isostatic pressing parameters, and performing hot isostatic pressing on the GH4099 superalloy formed by laser selective zone melting based on the hot isostatic pressing parameters so as to eliminate the defect that the GH4099 superalloy is internally influenced by the density of the GH4099 superalloy; setting a solution treatment parameter and an aging treatment parameter, and carrying out solution treatment on the GH4099 high-temperature alloy based on the solution treatment parameter and aging treatment on the GH4099 high-temperature alloy based on the aging treatment parameter to obtain the treated GH4099 high-temperature alloy. The application solves the technical problem that the performance of the GH4099 superalloy formed by selective laser melting in the prior art can not meet the actual requirements.
Description
Technical Field
The application relates to the technical field of material processing, in particular to a heat treatment method for forming GH4099 high-temperature alloy by selective laser melting.
Background
GH4099 is a typical nickel-based superalloy and has excellent high-temperature mechanical properties, creep resistance and corrosion resistance. The GH4099 superalloy has good high-temperature mechanical property after solution aging treatment, can be used for a long time below 900 ℃, has the highest working temperature of 1000 ℃, and is an important metal material in the aerospace field. The GH4099 alloy mainly uses Ni and Cr elements, performs solid solution strengthening by elements such as W, mo and Co, performs aging strengthening by Al and Ti, performs grain boundary strengthening by B, forms a complex structure which takes gamma phase as a matrix and contains other compound phases after solid solution and aging treatment, and can meet the use requirement of an aerospace high-temperature structural member. The laser selective melting forming technology is an additive manufacturing technology which takes laser as an energy source, continuously melts and solidifies metal powder and stacks the metal powder layer by layer to obtain a product, has the advantages of high efficiency, high precision, high design freedom degree and low cost, can form high-temperature alloy, titanium alloy, aluminum alloy and other materials, and has been widely applied in the aerospace field at present.
The GH4099 high-temperature alloy formed by laser selective melting can be applied to high-temperature structural members such as rudder wings, engine combustion chambers and the like. The GH4099 superalloy obtained through laser selective zone melting forming is a deposited GH4099 superalloy, and defects such as holes, microcracks and the like exist in the deposited GH4099 superalloy, so that the density of the alloy is reduced, stress concentration occurs when a structural member is in service, the stress is concentrated and becomes a crack source, and the strength, plasticity and fatigue performance of the structural member are reduced. In addition, the deposited GH4099 superalloy is a submicron-level cellular structure, the structure is favorable for improving the room-temperature mechanical property of the alloy, but reduces the high-temperature strength and plasticity of the alloy, and can not meet the use requirements, as shown in fig. 1A and 1B, wherein fig. 1A shows a schematic diagram of the interior of the GH4099 superalloy formed by laser selective melting and perpendicular to the forming direction; FIG. 1B shows a schematic view of the laser selective melt forming of GH4099 superalloy interior parallel to the forming direction.
Disclosure of Invention
The application solves the technical problems that: aiming at the problem that the performance of the GH4099 superalloy formed by selective laser melting in the prior art can not meet the actual requirements. According to the scheme provided by the embodiment of the application, the defects of holes, microcracks and the like of the GH4099 high-temperature alloy formed by the selective laser melting are eliminated through the hot isostatic pressing treatment, the fineness of the GH4099 high-temperature alloy is improved, and the mechanical property of the alloy is improved; and/or the cellular structure of the GH4099 high-temperature alloy formed by melting the laser selective area is converted into a fine equiaxed crystal structure through solution treatment and time-efficient treatment, a large number of fine dispersed gamma' strengthening phases are formed in the matrix, the toughness and the plasticity of the GH4099 high-temperature alloy are improved, and the performance of the GH4099 high-temperature alloy is further improved.
In a first aspect, an embodiment of the present application provides a heat treatment method for forming a GH4099 superalloy by selective laser melting, the method comprising:
Setting hot isostatic pressing treatment parameters, and carrying out hot isostatic pressing treatment on the GH4099 superalloy formed by laser selective zone melting based on the hot isostatic pressing treatment parameters so as to eliminate the defect that the GH4099 superalloy affects the fineness of the GH4099 superalloy; and/or
Setting a solution treatment parameter and an aging treatment parameter, carrying out solution treatment on the GH4099 superalloy based on the solution treatment parameter and carrying out aging treatment on the GH4099 superalloy based on the aging treatment parameter to obtain the treated GH4099 superalloy.
Optionally, the hot isostatic pressing treatment parameters include: the hot isostatic pressing temperature, the pressure and the first heat preservation time, wherein the value range of the hot isostatic pressing temperature is 1000-1200 ℃, the value range of the first heat preservation time is 2-4 hours, and the value range of the pressure is 90-130 MPa;
The solid solution treatment parameters comprise a first heating rate, a first solid solution temperature, a second heat preservation time, a first cooling speed and a first vacuum degree; the first heating rate is 2-15 ℃/min, the first solid solution temperature is 1100-1300 ℃, the second heat preservation time is 1-3 hours, the first cooling rate is 55-120 ℃/min, and the first vacuum degree precision is 10 -2 Pa.
The aging treatment parameters comprise a second heating rate, a second solid solution temperature, a third heat preservation time, a second cooling speed and a second vacuum degree; the second heating rate is 5-10 ℃/min, the second solid solution temperature is 720-780 ℃, the third heat preservation time is 6-10 hours, the second cooling rate is 10-20 ℃/min, and the second vacuum degree precision is 10 -2 Pa.
Optionally, the hot isostatic pressing temperature is set to 1050 ℃, the pressure is 90MPa, and the first heat preservation is performed for 2 hours.
Optionally, the hot isostatic pressing temperature is set to 1200 ℃, the pressure is 100MPa, and the first heat preservation is performed for 3 hours.
Optionally, performing hot isostatic pressing treatment on the selected laser zone-melting forming GH4099 superalloy based on the hot isostatic pressing treatment parameters, including:
setting the temperature in a high-temperature high-pressure sealing container for realizing hot isostatic pressing treatment to 1200 ℃ and the pressure to 100MPa;
Placing the GH4099 superalloy in the high-temperature high-pressure sealed container, and preserving heat for 3 hours to realize hot isostatic pressing treatment of the GH4099 superalloy.
Optionally, performing solution treatment on the GH4099 superalloy based on the solution treatment parameters comprises: and converting the submicron-order cellular structure in the GH4099 superalloy into an axillary structure.
Optionally, the first heating rate is set to be 2 ℃/min, the first solid solution temperature is 1100 ℃, the second heat preservation time is 1 hour, the first cooling rate is 55 ℃/min, and the first vacuum degree is 5×10 -2 Pa.
Optionally, the first heating rate is set to be 5 ℃/min, the first solid solution temperature is 1250 ℃, the second heat preservation time is 1.5 hours, the first cooling rate is 65 ℃/min, and the first vacuum degree is 5×10 - 2 Pa.
Optionally, the second heating rate is set to be 5 ℃/min, the second solid solution temperature is set to be 720 ℃, the third heat preservation time is set to be 6 hours, the second cooling rate is set to be 10 ℃/min, and the second vacuum degree precision is 5×10 -2 Pa.
Optionally, the second heating rate is set to be 5 ℃/min, the second solid solution temperature is set to be 730 ℃, the third heat preservation time is set to be 7 hours, the second cooling rate is set to be 10 ℃/min, and the second vacuum degree precision is 5×10 -2 Pa.
In the scheme provided by the embodiment of the application, the defects of holes, microcracks and the like of the GH4099 high-temperature alloy formed by melting the laser selected area are eliminated through hot isostatic pressing, the fineness of the GH4099 high-temperature alloy is improved, and the mechanical property of the alloy is improved; and/or the cellular structure of the GH4099 high-temperature alloy formed by melting the laser selective area is converted into a fine equiaxed crystal structure through solution treatment and time-efficient treatment, a large number of fine dispersed gamma' strengthening phases are formed in the matrix, the toughness and the plasticity of the GH4099 high-temperature alloy are improved, and the performance of the GH4099 high-temperature alloy is further improved.
Drawings
FIG. 1A shows a schematic view of the interior of a laser selective melt formed GH4099 superalloy perpendicular to the forming direction;
FIG. 1B shows a schematic view of the interior of a laser selective melt formed GH4099 superalloy parallel to the forming direction;
fig. 2 is a schematic flow chart of a heat treatment method for forming a GH4099 superalloy by selective laser melting according to an embodiment of the present application.
Detailed Description
In the solutions provided by the embodiments of the present application, the described embodiments are only some embodiments of the present application, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the application without making any inventive effort, are intended to be within the scope of the application.
In order to better understand the above technical solutions, the following detailed description of the technical solutions of the present application is made by using the accompanying drawings and specific embodiments, and it should be understood that the specific features of the embodiments and the embodiments of the present application are detailed descriptions of the technical solutions of the present application, and not limiting the technical solutions of the present application, and the technical features of the embodiments and the embodiments of the present application may be combined with each other without conflict.
The following describes in further detail a heat treatment method for forming a GH4099 superalloy by selective laser melting provided by the embodiment of the application with reference to the accompanying drawings, and the specific implementation manner of the method can include the following steps (the method flow is shown in fig. 2):
and 201, setting hot isostatic pressing parameters, and performing hot isostatic pressing on the GH4099 superalloy formed by laser selective zone melting based on the hot isostatic pressing parameters so as to eliminate the defect that the GH4099 superalloy is internally influenced by the fineness of the GH4099 superalloy.
As can be seen from fig. 1A and 1B, defects such as holes, bubbles, micro-cracks, etc. that affect the fineness of the GH4099 superalloy may exist in the GH4099 superalloy obtained by the laser selective melt forming technique. Whereas the hot isostatic pressing technique is one of the modern forming techniques of materials, which is a branch of the isostatic pressing technique. Isostatic pressing technology is generally classified into cold isostatic pressing, warm isostatic pressing and hot isostatic pressing according to the forming and consolidation temperatures. In the hot isostatic pressing, in a high-temperature high-pressure sealed container, high-pressure gas is used as a medium, and isostatic pressures are applied to powder or a sintered blank (or part) to be compacted in the high-temperature high-pressure sealed container to form a high-density blank or part.
Since the hot isostatic pressing is performed in a high-temperature and high-pressure sealed container, when performing hot isostatic pressing on a GH4099 superalloy formed by laser selective melting, parameters of the hot isostatic pressing, for example, environmental parameters in the high-temperature and high-pressure sealed container (such as temperature and pressure in the high-temperature and high-pressure sealed container when performing the hot isostatic pressing) and/or other parameters (such as time parameters) need to be set.
By way of example, setting the hot isostatic pressing parameters includes: the hot isostatic pressing temperature, the pressure and the first heat preservation time, wherein the value range of the hot isostatic pressing temperature is 1000-1200 ℃, the value range of the first heat preservation time is 2-4 hours, and the value range of the pressure is 90-130 MPa;
By way of further example, the hot isostatic pressing temperature is set at 1050 ℃, the pressure is 90MPa, and the first incubation is for 2 hours. Or setting the hot isostatic pressing temperature to 1200 ℃, setting the pressure to 100MPa, and setting the first heat preservation time to 3 hours.
As another example, performing hot isostatic pressing on a selected laser zone-melting forming GH4099 superalloy based on the hot isostatic pressing parameters comprises: setting the temperature in a high-temperature high-pressure sealing container for realizing hot isostatic pressing treatment to 1200 ℃ and the pressure to 100MPa; placing the GH4099 superalloy in the high-temperature high-pressure sealed container, and preserving heat for 3 hours to realize hot isostatic pressing treatment of the GH4099 superalloy.
Further, the defect that the density of the GH4099 superalloy is influenced inside the GH4099 superalloy can be eliminated by carrying out hot isostatic pressing treatment on the GH4099 superalloy formed by selective laser melting, so that the density of the GH4099 superalloy is improved.
And 202, setting solution treatment parameters and ageing treatment parameters, carrying out solution treatment on the GH4099 superalloy based on the solution treatment parameters and ageing treatment on the GH4099 superalloy based on the ageing treatment parameters to obtain the treated GH4099 superalloy.
In the scheme provided by the embodiment of the application, the GH4099 high-temperature alloy formed by laser selective melting is a submicron-level cellular structure, and the structure is favorable for improving the room-temperature mechanical property of the alloy, but reduces the high-temperature strength and plasticity of the alloy, and cannot meet the use requirement. Therefore, in order to improve the high-temperature strength and plasticity of the GH4099 superalloy, solid solution treatment and time-efficient treatment of the GH4099 superalloy are also required. The following is a brief description of the solution treatment and aging treatment processes, respectively, for the sake of easy understanding.
1. Solution treatment of
The solution treatment is a heat treatment process for heating the alloy to a high temperature in a single region and keeping the temperature constant, so that the excessive phase is fully dissolved into the solid solution and then is rapidly cooled to obtain the supersaturated solid solution. The solution treatment makes various phases in the alloy fully dissolved, strengthens solid solution, improves and enhances the plasticity and toughness of the alloy, eliminates stress and softening, and is prepared for precipitation hardening treatment.
Further, in order to achieve the solution treatment, it is necessary to set the solution treatment parameters. The solution treatment parameters include, for example, a first heating rate, a first solution temperature, a second hold time, a first cooling rate, and a first vacuum; the first heating rate is 2-15 ℃/min, the first solid solution temperature is 1100-1300 ℃, the second heat preservation time is 1-3 hours, the first cooling rate is 55-120 ℃/min, and the first vacuum degree precision is 10 -2 Pa.
As an example, the first heating rate is set to 2 ℃/min, the first solid solution temperature is 1100 ℃, the second holding time is 1 hour, the first cooling rate is 55 ℃/min, and the first vacuum degree is 5×10 -2 Pa. As another example, the first heating rate is set to 5 ℃/min, the first solid solution temperature is set to 1250 ℃, the second heat preservation time is set to 1.5 hours, the first cooling rate is set to 65 ℃/min, and the first vacuum degree is set to 5×10 -2 Pa.
2. Aging treatment
Aging treatment refers to a heat treatment process of the alloy workpiece, wherein the alloy workpiece is subjected to solution treatment, cold plastic deformation or casting and forging, and then is placed at a higher temperature or at room temperature, and the performance, shape and size of the alloy workpiece change with time. The aging treatment aims to eliminate internal stress of the workpiece, stabilize the structure and the size and improve the mechanical property.
Further, in order to achieve the aging treatment, it is necessary to set aging treatment parameters. The ageing treatment parameters comprise, for example, a second heating rate, a second solid solution temperature, a third holding time, a second cooling rate and a second vacuum degree; the second heating rate is 5-10 ℃/min, the second solid solution temperature is 720-780 ℃, the third heat preservation time is 6-10 hours, the second cooling rate is 10-20 ℃/min, and the second vacuum degree precision is 10-2Pa.
As an example, the second heating rate is set to be 5 ℃/min, the second solid solution temperature is set to be 720 ℃, the third heat preservation time is set to be 6 hours, the second cooling rate is set to be 10 ℃/min, and the second vacuum degree precision is set to be 5×10 -2 Pa. As another example, the second heating rate is set to be 5 ℃/min, the second solid solution temperature is set to be 730 ℃, the third heat preservation time is set to be 7 hours, the second cooling rate is set to be 10 ℃/min, and the second vacuum degree precision is set to be 5×10 -2 Pa.
The submicron cellular structure in the GH4099 superalloy is converted into fine equiaxed crystals through solution aging treatment, and fine dispersed gamma' strengthening phases are formed in the matrix, so that a laser selective melting forming GH4099 superalloy product with excellent room temperature and high temperature mechanical properties is obtained.
In the scheme provided by the embodiment of the application, the GH4099 superalloy hot isostatic pressing treatment, the solution treatment and the time-efficient treatment can be singly used according to actual needs or requirements, and can also be used in combination without limitation. In addition, for the hot isostatic pressing treatment, the solution treatment and the time-efficient treatment of the GH4099 superalloy, different treatment parameters can be set according to actual requirements, and the performance of the treated GH4099 superalloy obtained by aiming at the different treatment parameters is also different.
By way of example, performing hot isostatic pressing treatment on a GH4099 high-temperature alloy formed by laser selective melting, wherein the hot isostatic pressing temperature is 1050 ℃, the heat preservation time is 2h, and the pressure is 90MPa; carrying out solution treatment on the GH4099 high-temperature alloy formed by selective laser melting, wherein the heating rate is 2 ℃/min, the solution temperature is 1100 ℃, the heat preservation time is 1h, the cooling rate is 55 ℃/min, and the vacuum degree is 5 multiplied by 10 -2 Pa; and (3) carrying out aging treatment on the GH4099 high-temperature alloy formed by selective laser melting, wherein the heating rate is 5 ℃/min, the solid solution temperature is 720 ℃, the heat preservation time is 6h, the cooling rate is 10 ℃/min, and the vacuum degree is 5 multiplied by 10 -2 Pa. Experiments prove that under the treatment parameters, the density of the GH4099 high-temperature alloy formed by the laser selective zone melting of the strengthening heat treatment is 99.99%, the room-temperature tensile strength of the alloy is 1120MPa, the yield strength is 813MPa, the elongation is 31%, the tensile strength at 950 ℃ is 306MPa, the yield strength is 223MPa, and the elongation is 23%.
As another example, performing hot isostatic pressing treatment on the GH4099 high-temperature alloy formed by selective laser melting, wherein the hot isostatic pressing temperature is 1200 ℃, the heat preservation time is 3 hours, and the pressure is 100MPa; carrying out solution treatment on the GH4099 high-temperature alloy formed by selective laser melting, wherein the heating rate is 5 ℃/min, the solution temperature is 1250 ℃, the heat preservation time is 1.5h, the cooling rate is 65 ℃/min, and the vacuum degree is 5 multiplied by 10 -2 Pa; and (3) carrying out aging treatment on the GH4099 high-temperature alloy formed by selective laser melting, wherein the heating rate is 5 ℃/min, the solid solution temperature is 730 ℃, the heat preservation time is 7h, the cooling rate is 10 ℃/min, and the vacuum degree is 5 multiplied by 10 -2 Pa. Experiments prove that the density of the GH4099 high-temperature alloy formed by the laser selective zone melting of the strengthening heat treatment under the treatment parameters is 99.99%, the room-temperature tensile strength of the alloy is 1150MPa, the yield strength is 825MPa, the elongation is 33%, the tensile strength at 950 ℃ is 310MPa, the yield strength is 215MPa, and the elongation is 21%.
In the scheme provided by the embodiment of the application, the defects of holes, microcracks and the like of the GH4099 high-temperature alloy formed by melting the laser selected area are eliminated through hot isostatic pressing, the fineness of the GH4099 high-temperature alloy is improved, and the mechanical property of the alloy is improved; and/or the cellular structure of the GH4099 high-temperature alloy formed by melting the laser selective area is converted into a fine equiaxed crystal structure through solution treatment and time-efficient treatment, a large number of fine dispersed gamma' strengthening phases are formed in the matrix, the toughness and the plasticity of the GH4099 high-temperature alloy are improved, and the performance of the GH4099 high-temperature alloy is further improved.
It will be appreciated by those skilled in the art that embodiments of the present application may be provided as a method, system, or computer program product. Accordingly, the present application may take the form of an entirely hardware embodiment, an entirely software embodiment or an embodiment combining software and hardware aspects. Furthermore, the present application may take the form of a computer program product embodied on one or more computer-usable storage media (including, but not limited to, magnetic disk storage, optical storage, and the like) having computer-usable program code embodied therein.
The present application is described with reference to flowchart illustrations and/or block diagrams of methods, apparatus (systems) and computer program products according to embodiments of the application. It will be understood that each flow and/or block of the flowchart illustrations and/or block diagrams, and combinations of flows and/or blocks in the flowchart illustrations and/or block diagrams, can be implemented by computer program instructions. These computer program instructions may be provided to a processor of a general purpose computer, special purpose computer, embedded processor, or other programmable data processing apparatus to produce a machine, such that the instructions, which execute via the processor of the computer or other programmable data processing apparatus, create means for implementing the functions specified in the flowchart flow or flows and/or block diagram block or blocks.
These computer program instructions may also be stored in a computer-readable memory that can direct a computer or other programmable data processing apparatus to function in a particular manner, such that the instructions stored in the computer-readable memory produce an article of manufacture including instruction means which implement the function specified in the flowchart flow or flows and/or block diagram block or blocks.
These computer program instructions may also be loaded onto a computer or other programmable data processing apparatus to cause a series of operational steps to be performed on the computer or other programmable apparatus to produce a computer implemented process such that the instructions which execute on the computer or other programmable apparatus provide steps for implementing the functions specified in the flowchart flow or flows and/or block diagram block or blocks.
It will be apparent to those skilled in the art that various modifications and variations can be made to the present application without departing from the spirit or scope of the application. Thus, it is intended that the present application also include such modifications and alterations insofar as they come within the scope of the appended claims or the equivalents thereof.
Claims (9)
1. A heat treatment method for forming GH4099 superalloy by laser selective melting, which is characterized by comprising the following steps:
Setting hot isostatic pressing treatment parameters, and carrying out hot isostatic pressing treatment on the GH4099 superalloy formed by laser selective zone melting based on the hot isostatic pressing treatment parameters so as to eliminate the defect that the GH4099 superalloy affects the fineness of the GH4099 superalloy; and/or
Setting a solution treatment parameter and an aging treatment parameter, carrying out solution treatment on the GH4099 superalloy based on the solution treatment parameter and carrying out aging treatment on the GH4099 superalloy based on the aging treatment parameter to obtain a treated GH4099 superalloy;
the cellular structure of the GH4099 high-temperature alloy formed by selective laser melting is converted into a fine equiaxed crystal structure, and a large amount of fine dispersed gamma' strengthening phases are formed in the matrix;
the hot isostatic pressing treatment parameters include: the hot isostatic pressing temperature, the pressure and the first heat preservation time, wherein the value range of the hot isostatic pressing temperature is 1000-1200 ℃, the value range of the first heat preservation time is 2-4 hours, and the value range of the pressure is 90 MPa-130 MPa;
The solid solution treatment parameters comprise a first heating rate, a first solid solution temperature, a second heat preservation time, a first cooling speed and a first vacuum degree; the first heating rate is 2-15 ℃/min, the first solid solution temperature is 1100-1300 ℃, the second heat preservation time is 1-3 hours, the first cooling rate is 55-120 ℃/min, and the first vacuum degree precision is 10 -2 Pa;
The aging treatment parameters comprise a second heating rate, a second solid solution temperature, a third heat preservation time, a second cooling speed and a second vacuum degree; the second heating rate is 5-10 ℃/min, the second solid solution temperature is 720-780 ℃, the third heat preservation time is 6-10 hours, the second cooling rate is 10-20 ℃/min, and the second vacuum degree precision is 10 -2 Pa.
2. The method of claim 1, wherein the hot isostatic pressing temperature is set at 1050 ℃, the pressure is 90 MPa, and the first soak is 2 hours.
3. The method of claim 1, wherein the hot isostatic pressing temperature is set at 1200 ℃, the pressure is 100 MPa, and the first soak is 3 hours.
4. The method of claim 2, wherein performing a hot isostatic pressing process on the laser selective melt formed GH4099 superalloy based on the hot isostatic pressing parameters comprises:
setting the temperature in a high-temperature high-pressure sealed container for realizing hot isostatic pressing treatment to be 1200 ℃ and the pressure to be 100 MPa;
Placing the GH4099 superalloy in the high-temperature high-pressure sealed container, and preserving heat for 3 hours to realize hot isostatic pressing treatment of the GH4099 superalloy.
5. The method of any one of claims 1-4, wherein solution treating the GH4099 superalloy based on the solution treatment parameters comprises:
and converting the submicron-order cellular structure in the GH4099 superalloy into an axillary structure.
6. The method of any one of claims 1-4, wherein the first heating rate is set to 2 ℃/min, the first solid solution temperature is 1100 ℃, the second holding time is 1 hour, the first cooling rate is 55 ℃/min, and the first vacuum is 5 x 10 -2 Pa.
7. The method of any one of claims 1-4, wherein the first heating rate is set to 5 ℃/min, the first solid solution temperature is 1250 ℃, the second holding time is 1.5 hours, the first cooling rate is 65 ℃/min, and the first vacuum is 5 x 10 -2 Pa.
8. The method of any one of claims 1-4, wherein the second heating rate is set to a value of 5 ℃/min, the second solution temperature is set to a value of 720 ℃, the third holding time is set to a value of 6 hours, the second cooling rate is set to a value of 10 ℃/min, and the second vacuum degree precision is 5 x 10 -2 Pa.
9. The method of any one of claims 1-4, wherein the second heating rate is set to a value of 5 ℃/min, the second solution temperature is set to a value of 730 ℃, the third holding time is set to a value of 7 hours, the second cooling rate is set to a value of 10 ℃/min, and the second vacuum degree precision is 5 x 10 -2 Pa.
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