CN113996805A - GH4169 high-temperature alloy ingot casting forming method - Google Patents
GH4169 high-temperature alloy ingot casting forming method Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
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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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- 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
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/66—Treatment of workpieces or articles after build-up by mechanical means
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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
- B33Y80/00—Products made by 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
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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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 relates to a GH4169 high-temperature alloy ingot forming method, which prepares a GH4169 alloy oversized ingot by a laser casting additive manufacturing method, and the average chemical composition of the GH4169 alloy oversized ingot is 52.5Ni-19.0Cr-5.13Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%). The laser power for forming is 280-290W, the scanning speed is 950-970mm/s, the scanning pitch is 79-81 μm, the layer thickness is 39-41 μm, and the interlayer rotation angle is 17-25 deg. The alloy matrix is gamma phase, no obvious precipitated phase exists in the crystal and on the crystal boundary, the dendrite in the crystal is fine, and the dendrite segregation is mainly Nb. The GH4169 alloy cast ingot prepared by the additive manufacturing and forming method is low in segregation coefficient, and compared with the traditional cast alloy, the GH4169 alloy cast ingot can be directly cogging without homogenization heat treatment. The cogging deformation activation energy of the alloy is lower than that of the traditional casting GH4169 alloy, and the alloy does not crack in the cogging process and has excellent cogging performance.
Description
Technical Field
The invention belongs to the field of high-temperature alloys, and particularly relates to a forming method for preparing a GH4169 high-temperature alloy ingot with an oversized diameter.
Background
At present, GH4169 is a precipitation-strengthened nickel-based high-temperature alloy, has good comprehensive performance within the temperature range of-253 ℃ to 650 ℃, has good yield strength below 650 ℃, and has good fatigue resistance, radiation resistance, oxidation resistance, corrosion resistance, good processability and good welding performance. Can manufacture various parts with complex shapes, and has wide application in aerospace, nuclear energy, petroleum industry and extrusion dies in the temperature range.
The GH4169 alloy smelted by the traditional method has a coarse dendritic structure and serious dendritic segregation, so that homogenization is difficult, but homogenization treatment is required to eliminate dendritic crystals. Moreover, the precipitated phases of the alloy are complex, the Laves phase, MC carbide and delta phase exist in the as-cast GH4169 alloy, and after the homogenization heat treatment, the Laves phase can be eliminated, but the delta phase grows and dissolves back, particularly the grain structure becomes coarse, and the recrystallization capability of the alloy in the cogging process is reduced. The segregation degree of the core and the edge of the traditional GH4169 ingot is different, the segregation degree of the core is higher, and in order to make the core fully uniform during heat treatment, the precipitated phase at the edge is grown up or dissolved back, and the cogging performance of the alloy is also reduced. As shown in figure 1, GH4169 alloy prepared by the traditional casting method has coarse dendrites, developed secondary dendrite arms and a large amount of precipitated phases among dendrites, including granular Laves phases and acicular delta phases, and is not beneficial to the cogging performance of the alloy.
Disclosure of Invention
The invention discloses a GH4169 high-temperature alloy ingot forming method, which solves any one of the technical problems and other potential problems in the prior art.
In order to solve the technical problems, the technical scheme of the invention is as follows: a GH4169 high-temperature alloy ingot forming method comprises the following steps:
s1) designing GH4169 high-temperature alloy components, mixing the components and uniformly mixing;
s2) molding the mixed material obtained in the step S1) by adopting a laser casting additive manufacturing method to obtain an alloy casting blank;
s3) carrying out deformation treatment on the alloy casting blank obtained in the step S2) at a certain temperature to finally obtain a GH4169 high-temperature alloy ingot.
Further, the GH4169 superalloy in S1) has the chemical composition of 52.5Ni-19.0Cr-5.13Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%).
Further, the molding process in S2) specifically includes:
the laser power is 280-290W, the scanning speed is 950-970mm/s, the scanning interval is 79-81 mu m, the layer thickness is 39-41 mu m, and the interlaminar rotation angle is 17-25 degrees, so as to obtain the alloy casting blank.
Furthermore, the microstructure of the alloy casting blank has wavy lines, crystal grains grow across the boundary of the molten pool, and the growth direction of the crystal grains is consistent with the heat flow direction during solidification.
Further, the specific process of S3) is as follows: the temperature is 1000-1100 ℃, and the strain rate is 0.1-10 s-1And the deformation amount is 30-60%.
Furthermore, the alloy matrix of the GH4169 high-temperature alloy ingot is a gamma phase, no obvious precipitated phase exists in the crystal interior and on the crystal boundary, the dendrite in the crystal interior is fine, and the dendrite segregation is Nb element.
An GH4169 superalloy ingot formed by the forming method of any of claims 1 to 7.
The invention has the beneficial effects that: by adopting the technical scheme, the alloy matrix formed by the method is a gamma phase, no obvious precipitated phase exists in the crystal and on the crystal boundary, the dendrite in the crystal is fine, and the dendrite segregation is mainly Nb. The GH4169 alloy cast ingot prepared by the additive manufacturing and forming method is low in segregation coefficient, and compared with the traditional cast alloy, the GH4169 alloy cast ingot can be directly cogging without homogenization heat treatment. The cogging deformation activation energy of the alloy is lower than that of the traditional casting GH4169 alloy, and the alloy does not crack in the cogging process and has excellent cogging performance.
Drawings
FIG. 1 is a schematic structural morphology of GH4169 alloy cast by a conventional method.
FIG. 2 is a schematic structural morphology of GH4169 alloy manufactured by adopting laser additive manufacturing according to the invention.
FIG. 3a is a schematic diagram of the macro topography of the sample before deformation.
FIG. 3b is a schematic diagram of the macro topography of the sample after deformation.
FIG. 4a shows that the deformation rate of the additive manufactured GH4169 alloy is 0.1s-1Schematic diagram of true stress-true strain curve.
FIG. 4b is an additive manufactured GH4169 alloy at a deformation rate of 1s-1Schematic diagram of true stress-true strain curve.
FIG. 5 is a hot working drawing of additive manufactured GH4169 alloy at different strains.
FIG. 6a is a 200 XIPF plot of the GH4169 alloy in its as-received state.
FIG. 6b is a 300 IPF plot of the GH4169 alloy after deformation.
FIG. 6c is a 2000x IPF plot of the GH4169 alloy after deformation.
Detailed Description
The technical solution of the present invention is further explained below with reference to the specific embodiments and the accompanying drawings.
The invention discloses a GH4169 high-temperature alloy ingot casting forming method, which comprises the following steps:
s1), designing GH4169 high-temperature alloy components, pulverizing, mixing and uniformly mixing;
s2) molding the mixed material obtained in the step S1) by adopting a laser casting additive manufacturing method to obtain an alloy casting blank;
s3) carrying out deformation treatment on the alloy casting blank obtained in the step S2) at a certain temperature to finally obtain a GH4169 high-temperature alloy ingot.
The GH4169 superalloy in S1) has the chemical composition of 52.5Ni-19.0Cr-5.13Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%).
The molding process in S2) specifically includes:
the laser power is 280-290W, the scanning speed is 950-970mm/s, the scanning interval is 79-81 mu m, the layer thickness is 39-41 mu m, and the interlaminar rotation angle is 17-25 degrees, so as to obtain the alloy casting blank.
The microstructure of the alloy casting blank has wavy lines, crystal grains grow across the boundary of a molten pool, and the growth direction is consistent with the heat flow direction during solidification.
The S3) specific process comprises the following steps: the temperature is 1000-1100 ℃, and the strain rate is 0.1-10 s-1And the deformation amount is 30-60%.
The alloy matrix of the GH4169 high-temperature alloy ingot is a gamma phase, no obvious precipitated phase exists in the crystal interior and on the crystal boundary, the dendrite in the crystal interior is fine, the dendrite is segregated into Nb, and the Nb segregation coefficient is 1.70.
The deformation activation energy of the GH4169 high-temperature alloy ingot is 350-475kJ & mol-1，。
The GH4169 high-temperature alloy cast ingot is obtained by molding the GH4169 high-temperature alloy cast ingot by the molding method.
Example 1:
the GH4169 high-temperature alloy comprises the following chemical components: 52.5Ni-19.0Cr-5.13Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%),
the GH4169 alloy prepared by the method (forming laser process parameters: power 285W, scanning speed 960mm/s, scanning interval 80 μm, layer thickness 40 μm and interlayer rotation angle 17 ℃) has a structure appearance under a light mirror, as shown in figure 2, wavy lines are molten pool boundary appearances left by laser casting metal powder, crystal grains grow across the molten pool boundaries, and the growth direction of the crystal grains is consistent with the heat flow direction during solidification.
Mass fractions of elements between dendrite trunks and dendrite dendrites of additive-fabricated GH4169 alloys were measured using EDS analysis and the results are listed in table 1. It was found that segregation of Nb element was present in the dendrite, the Nb segregation coefficient was 1.70, and segregation of other elements was not significant.
Table 1 additive manufacturing GH4169 dendrite segregation results
The additive manufacturing GH4169 alloy shown in FIG. 3(a) is directly subjected to cogging, and a thermal compression test is carried out on a Gleeble-3500 testing machine, wherein the testing temperature is 1000-1100 ℃, and the strain rate is 0.1s-1The deformation amounts were all 50%, and the specific test conditions are shown in table 2. As shown in FIG. 3(b), the sample after the test was deformed uniformly and was not cracked after the deformation.
The true stress-true strain curves of the thermal compression test are shown in fig. 4a and 4b, and it can be found that the stress level shows a tendency to decrease as the strain rate decreases with an increase in the deformation temperature.
From the test results of the thermal deformation, a hot working diagram for additive manufacturing of GH4169 alloy was derived (fig. 5). The derivation results show that under the test conditions, no instability region exists, the instability region is consistent with the cracking phenomenon of the tested sample, and the GH4169 alloy prepared by the additive manufacturing method has good direct cogging performance. The peak value of the power dissipation coefficient is between the low strain rate and 1040-1080 ℃, and the high strain rate area is expanded along with the increase of the strain quantity.
According to the test result of the thermal deformation, the constitutive equation of the GH4169 alloy is deduced:
as can be seen from the equation, the activation energy for thermal deformation is 429.772kJ · mol-1Table 3 shows the results of comparing the direct cogging of the GH4169 alloy prepared by the additive manufacturing method with the direct cogging of the GH4169 alloy prepared by the conventional casting method and the deformation activation energy of the homogenized direct cogging.
TABLE 3 deformation activation energy of GH4169 alloy at various positions and after homogenization in the As-cast state
The comparison result in table 2 shows that although the thermal deformation activation energy of the GH4169 alloy prepared by the additive manufacturing method is higher than that after the homogenization treatment in the as-cast state, the thermal deformation activation energy is 21.5% lower than that of the center of the as-cast state, 24.2% lower than that of the R/2 position of the as-cast state, and 28.4% lower than that of the edge of the as-cast state, which indicates that the preparation method is obviously easier than the cogging in the as-cast state, can directly perform the cogging without homogenization treatment, and saves time and cost.
An IPF graph of EBSD analysis results of the additive manufactured GH4169 alloy in the original state and the sample after thermal deformation is shown in FIG. 6. It can be clearly observed that the original additive manufactured grains are broken and recrystallized to form fine recrystallized grains, and the recrystallized regions are interconnected. The higher the deformation temperature, the larger the recrystallized region fraction.
Example 2:
the GH4169 high-temperature alloy comprises the following chemical components: 52.5Ni-19.0Cr-5.10Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%),
the GH4169 alloy prepared by the preparation process additive manufacturing method (the forming laser process parameters are that the power is 285W, the scanning speed is 970mm/s, the scanning interval is 80 mu m, the layer thickness is 40 mu m, and the interlayer rotation angle is 20 degrees) has a wavy texture, the morphology of the molten pool boundary is left by laser casting metal powder, crystal grains grow across the molten pool boundary, and the growth direction of the crystal grains is consistent with the heat flow direction during solidification.
The additive manufacturing GH4169 alloy is directly subjected to cogging, the test temperature is 1050 ℃, and the strain rate is 5s-1The deformation is 50%, the sample after the test is deformed uniformly, and no crack is generated after the deformation. The GH4169 alloy prepared by the additive manufacturing method is obviously easier than the traditional as-cast cogging, can be directly cogging without homogenization treatment, and saves time and cost.
Example 3:
the GH4169 high-temperature alloy comprises the following chemical components: 52.5Ni-19.0Cr-4.75Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%),
the GH4169 alloy prepared by the preparation process additive manufacturing method (the forming laser process parameters are 285W, the scanning speed is 955mm/s, the scanning interval is 81 mu m, the layer thickness is 39 mu m, and the interlayer rotation angle is 25 degrees) has a wavy texture, the morphology of the molten pool boundary remained by the laser casting metal powder is the morphology of the molten pool boundary, crystal grains grow across the molten pool boundary, and the growth direction of the crystal grains is consistent with the heat flow direction during solidification.
The additive manufactured GH4169 alloy is directly subjected to cogging, the test temperature is 1000 ℃, and the strain rate is 6s-1The deformation is 60%, the sample after the test is deformed uniformly, and the sample is not cracked after being deformed. The GH4169 alloy prepared by the additive manufacturing method is obviously easier than the traditional as-cast cogging, can be directly cogging without homogenization treatment, and saves time and cost.
Example 4:
the GH4169 high-temperature alloy comprises the following chemical components: 52.5Ni-19.0Cr-5.55Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%),
the GH4169 alloy prepared by the preparation process additive manufacturing method (the forming laser process parameters are 285W, the scanning speed is 950mm/s, the scanning distance is 79 mu m, the layer thickness is 41 mu m, and the interlayer rotation angle is 22 degrees) has a wavy texture, the morphology of the molten pool boundary remained by the laser casting metal powder is the morphology of the molten pool boundary, crystal grains grow across the molten pool boundary, and the growth direction of the crystal grains is consistent with the heat flow direction during solidification.
The additive manufactured GH4169 alloy is directly subjected to cogging, the test temperature is 1100 ℃, and the strain rate is 1s-1The deformation is 55%, the sample after the test is deformed uniformly, and no crack is generated after the deformation. The GH4169 alloy prepared by the additive manufacturing method is obviously easier than the traditional as-cast cogging, can be directly cogging without homogenization treatment, and saves time and cost.
The details of the GH4169 high-temperature alloy ingot forming method provided by the embodiment of the application are described above. The above description of the embodiments is only for the purpose of helping to understand the method of the present application and its core ideas; meanwhile, for a person skilled in the art, according to the idea of the present application, there may be variations in the specific embodiments and the application scope, and in summary, the content of the present specification should not be construed as a limitation to the present application.
As used in the specification and claims, certain terms are used to refer to particular components. As one skilled in the art will appreciate, manufacturers may refer to a component by different names. This specification and claims do not intend to distinguish between components that differ in name but not function. In the following description and in the claims, the terms "include" and "comprise" are used in an open-ended fashion, and thus should be interpreted to mean "include, but not limited to. "substantially" means within an acceptable error range, and a person skilled in the art can solve the technical problem within a certain error range to substantially achieve the technical effect. The description which follows is a preferred embodiment of the present application, but is made for the purpose of illustrating the general principles of the application and not for the purpose of limiting the scope of the application. The protection scope of the present application shall be subject to the definitions of the appended claims.
It is also noted that the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a good or system that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such good or system. Without further limitation, an element defined by the phrase "comprising an … …" does not exclude the presence of other like elements in a commodity or system that includes the element.
It should be understood that the term "and/or" as used herein is merely one type of association that describes an associated object, meaning that three relationships may exist, e.g., a and/or B may mean: a exists alone, A and B exist simultaneously, and B exists alone. In addition, the character "/" herein generally indicates that the former and latter related objects are in an "or" relationship.
The foregoing description shows and describes several preferred embodiments of the present application, but as aforementioned, it is to be understood that the application is not limited to the forms disclosed herein, but is not to be construed as excluding other embodiments and is capable of use in various other combinations, modifications, and environments and is capable of changes within the scope of the application as described herein, commensurate with the above teachings, or the skill or knowledge of the relevant art. And that modifications and variations may be effected by those skilled in the art without departing from the spirit and scope of the application, which is to be protected by the claims appended hereto.
Claims (8)
1. A GH4169 high-temperature alloy ingot casting forming method is characterized by comprising the following steps: the molding method comprises the following steps:
s1), designing GH4169 high-temperature alloy components, pulverizing, mixing and uniformly mixing;
s2) molding the mixed material obtained in the step S1) by adopting a laser casting additive manufacturing method to obtain an alloy casting blank;
s3) carrying out deformation treatment on the alloy casting blank obtained in the step S2) at a certain temperature to finally obtain a GH4169 high-temperature alloy casting ingot.
2. The molding method according to claim 1, wherein: the GH4169 superalloy in S1) has the chemical composition of 52.5Ni-19.0Cr-5.13Nb-3.05Mo-0.9Ti-0.5Al-0.05C-18.87Fe (wt%).
3. The molding method according to claim 1, wherein: the molding process in S2) specifically includes: the laser power is 280-290W, the scanning speed is 950-970mm/s, the scanning interval is 79-81 mu m, the layer thickness is 39-41 mu m, and the interlaminar rotation angle is 17-25 degrees, so as to obtain the alloy casting blank.
4. The molding method according to claim 3, wherein: the microstructure of the alloy casting blank has wavy lines, crystal grains grow across the boundary of a molten pool, and the growth direction is consistent with the heat flow direction during solidification.
5. The molding method according to claim 1, wherein: the S3) specific process comprises the following steps: the temperature is 1000-1100 ℃, and the strain rate is 0.1-10 s-1And the deformation amount is 30-60%.
6. The molding method according to claim 1, wherein: the alloy matrix of the GH4169 high-temperature alloy ingot is a gamma phase, no obvious precipitated phase exists in the crystal interior and on the crystal boundary, the dendrite in the crystal interior is fine, the dendrite is segregated into Nb, and the Nb segregation coefficient is 1.70.
7. The molding method according to claim 1, wherein: the deformation activation energy of the GH4169 high-temperature alloy ingot is 350-475kJ & mol-1，。
8. An GH4169 superalloy ingot formed by the forming method of any of claims 1 to 7.
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