CN112376003A - Process for improving yield strength of GH141 material - Google Patents

Process for improving yield strength of GH141 material Download PDF

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CN112376003A
CN112376003A CN202011158742.9A CN202011158742A CN112376003A CN 112376003 A CN112376003 A CN 112376003A CN 202011158742 A CN202011158742 A CN 202011158742A CN 112376003 A CN112376003 A CN 112376003A
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yield strength
cooling
treatment
temperature
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CN112376003B (en
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张磊
王玉锋
赵志雄
王军
孟涛
李庆
解保强
邓自强
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Northwestern Polytechnical University
AECC Aviation Power Co Ltd
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AECC Aviation Power Co Ltd
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K3/00—Tools, devices, or special appurtenances for soldering, e.g. brazing, or unsoldering, not specially adapted for particular methods
    • B23K3/08—Auxiliary devices therefor
    • B23K3/085—Cooling, heat sink or heat shielding means
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/16—Arc welding or cutting making use of shielding gas
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/32—Accessories
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum

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  • Mechanical Engineering (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Abstract

The invention discloses a process for improving yield strength of a GH141 material, and belongs to the field of alloy treatment. A process for increasing yield strength of a GH141 material, comprising: 1) carrying out annealing treatment and solid solution treatment on the GH141 material according to a standard process to obtain a supplied matrix structure; 2) performing high-temperature brazing treatment to obtain a high-temperature brazed matrix structure 3) performing heat treatment on the high-temperature brazed matrix structure, wherein the heat treatment conditions are as follows: at 5.0X 10‑2Heating to 830-860 ℃ below Pa air pressure, and keeping the temperature for 1-2 h; then cooling the furnace to 710-730 ℃, and preserving heat for 8-9 h; then the furnace is cooled to 610-630 ℃, and the heat preservation is 8 ℃9 h; then air cooling is carried out to below 80 ℃, and the heat treatment is completed. The process solves the problem of low yield strength index of the re-aging material caused by high-temperature brazing.

Description

Process for improving yield strength of GH141 material
Technical Field
The invention belongs to the field of alloy treatment, and particularly relates to a process for improving yield strength of a GH141 material.
Background
At present, precipitation hardening type nickel-based wrought superalloy (GH141 material) is widely applied in the industrial fields of aeroengines, combustion engines and the like, and the GH141 material is required to be subjected to main processes such as machining, welding, heat treatment and the like to finally form a required product.
The GH141 material needs to be subjected to complex forming procedures from blanks to finished products, such as machining, punch forming and the like, so that large residual stress is generated on parts. The welding process comprises high-temperature brazing, argon arc welding, electron beam welding and the like, welding stress is generated, the mechanical strength of a welding line and a base body is influenced, and finally, part deformation and service performance are greatly influenced.
The heat treatment standard of the traditional GH141 high-temperature alloy only stipulates the annealing, solid solution and aging of raw materials, and in order to prevent the oxidation of parts, the aging treatment adopts vacuum aging, and the specific process is as follows: and (3) preserving heat for 4 hours at 900 ℃, and cooling by using an argon (0.5-2 bar) fan. Because the pressure of the argon filled in the furnace is low, the cooling speed of cooling is slightly slower than that of air cooling, the yield strength after vacuum aging is in the required lower limit value, and the risk of unqualified yield strength exists. In addition, the brazing temperature of the GH141 material is high, the brazing temperature is between the solid solution temperature and the aging temperature, in order to prevent weld cracking, slow cooling is performed before argon gas rapid cooling during vacuum brazing, precipitation amount and size of a matrix strengthening phase gamma' of the GH141 material are affected, and final yield strength of the part after aging treatment is low.
Disclosure of Invention
The invention provides a process for improving yield strength of a GH141 material, aiming at overcoming the defect that the yield strength of the GH141 material treated by a standard process is lower.
In order to achieve the purpose, the invention adopts the following technical scheme to realize the purpose:
a process for improving yield strength of a GH141 material, comprising the steps of:
1) carrying out annealing treatment and solid solution treatment on the GH141 material according to a standard process to obtain a supplied matrix structure;
2) carrying out high-temperature brazing treatment on the supplied matrix structure obtained in the step 1) to obtain a matrix structure subjected to high-temperature brazing;
3) carrying out heat treatment on the matrix structure after high-temperature brazing obtained in the step 2), wherein the heat treatment conditions are as follows:
at 5.0X 10-2Heating to 830-860 ℃ below Pa air pressure, and keeping the temperature for 1-2 h;
then cooling the furnace to 710-730 ℃, and preserving heat for 8-9 h;
then cooling the furnace to 610-630 ℃, and preserving heat for 8-9 h;
then air cooling is carried out to below 80 ℃, and the heat treatment is completed.
Further, the air cooling operation in the step 3) is as follows:
argon gas was introduced with a blowing fan.
Further, the supplied base structure obtained in step 1) is directly subjected to the heat treatment described in step 3).
Further, the step 2) is as follows:
and (2) carrying out argon arc welding on the supplied matrix structure obtained in the step 1) to obtain the matrix structure after argon arc welding.
Further, the heat treatment conditions in step 3) are as follows:
at 4.0X 10-2Heating to 840 ℃ under the pressure of Pa, and preserving heat for 2 h;
then furnace cooling is carried out to 720 ℃, and heat preservation is carried out for 9 h;
then furnace cooling is carried out to 620 ℃, and heat preservation is carried out for 9 hours;
then argon is introduced and a blowing fan is used for cooling to 70 ℃.
Further, the heat treatment conditions in step 3) are as follows:
at 3.0X 10-2Heating to 840 ℃ under Pa, and preserving heat for 1 h;
then furnace cooling is carried out to 710 ℃, and heat preservation is carried out for 8 hours;
then furnace cooling is carried out to 610 ℃, and heat preservation is carried out for 8 hours;
then argon is introduced, and a blowing fan is used for cooling to 60 ℃, so that the heat treatment is completed.
Compared with the prior art, the invention has the following beneficial effects:
according to the process for improving the yield strength of the GH141 material, the GH141 material is subjected to annealing and solution treatment to obtain a supply state matrix, the supply state matrix is subjected to or not subjected to high-temperature brazing, then heat treatment is carried out, and vacuum aging of low temperature and long time is adopted, so that the yield strength of the material is improved, the residual stress is eliminated, and the deformation of parts is prevented; when the brazing treatment is not carried out, the yield strength of the obtained GH141 material is improved by 13-30%; after the brazing treatment is carried out, the yield strength of the obtained GH141 material is improved by 10-30%. The process for improving the yield strength of the GH141 material is not only beneficial to reducing the residual stress and the welding stress generated by machining, but also solves the problem of low yield strength index of the re-aged material caused by high-temperature brazing.
Drawings
FIG. 1 is an equilibrium phase diagram of a GH141 alloy;
FIG. 2 is an SEM image of GH141 alloy after solution treatment and aging treatment, wherein, FIGS. 2(a) and 2(b) are SEM images at different magnifications;
FIG. 3 is an SEM picture of GH141 alloy after high temperature brazing after solutionizing and aging, wherein FIG. 3(a),
FIG. 3(b) is an SEM image at different magnifications;
FIG. 4 is an SEM image of a GH141 alloy after high temperature brazing and after standard aging treatment;
FIG. 5 is an SEM image of GH141 alloy after the process of the invention.
Detailed Description
Technical solutions in embodiments of the present invention are clearly and completely described in order to enable those skilled in the art to better understand the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
It is noted that the terms first, second and the like in the description and in the claims of the present invention are used for distinguishing between similar elements and not necessarily for describing a particular sequential or chronological order. It is to be understood that the data so used are interchangeable under appropriate circumstances such that the embodiments of the invention described herein are capable of operation in sequences other than those described. Furthermore, the terms "comprises," "comprising," and "having," and any variations thereof, are intended to cover a non-exclusive inclusion, such that a process, method, system, article, or apparatus that comprises a list of steps or elements is not necessarily limited to those steps or elements expressly listed, but may include other steps or elements not expressly listed or inherent to such process, method, article, or apparatus.
Example 1
The process method for improving the strength of the high-temperature alloy GH141 material comprises the following specific implementation modes:
(1) carrying out annealing treatment and solution treatment on the part according to the material standard so as to obtain a supplied matrix structure;
(2) performing argon arc welding on the supplied matrix tissue obtained in the step 1);
(3) carrying out heat treatment on the welded supplied matrix structure, wherein the specific conditions of the heat treatment are as follows:
at 4.0X 10-2Heating the part to 840 ℃ under Pa, and preserving heat for 2h at 840 ℃;
then cooling to 720 ℃ in vacuum, and preserving heat for 9 h;
then cooling to 620 ℃ in vacuum, and preserving heat for 9 hours;
then high purity argon gas + fan cooling to 70 ℃.
The heat treatment is used for improving the yield strength of the GH141 material.
Table 1 shows the comparison of the data of the high-temperature tensile properties of the GH141 material after vacuum aging treatment, and in table 1, the data of the high-temperature tensile properties of the GH141 material after vacuum aging treatment are compared, and it can be seen from table 1 that the yield strength value of the high-temperature alloy GH141 material obtained after the heat treatment in example 1 is improved by 85MPa and the yield strength index is improved by 13.7% compared with the standard process method.
TABLE 1GH141 Material Performance data processed by Standard Process and example 1
Figure BDA0002743650360000051
Example 2
The process method for improving the strength of the high-temperature alloy GH141 material comprises the following specific implementation modes:
1) carrying out annealing treatment and solid solution treatment on the part or the sample according to the material standard to obtain a supplied matrix structure;
2) carrying out high-temperature brazing treatment on the supplied matrix tissue part to obtain a matrix tissue subjected to high-temperature brazing;
3) carrying out heat treatment on the part obtained in the step 2), wherein the heat treatment conditions are as follows:
at 3.0X 10-2Heating the part to 840 ℃ under Pa, and preserving heat for 1 h;
then vacuum cooling is carried out to 710 ℃, and heat preservation is carried out for 8 hours;
then vacuum cooling to 610 ℃, and preserving heat for 8 h;
then the mixture is cooled to 60 ℃ by introducing high-purity argon and a fan.
The heat treatment is used for improving the yield strength of the GH141 material.
In the table 2, the data of the high-temperature tensile property of the GH141 material subjected to vacuum aging treatment after brazing are compared, and it can be seen from the table that the tensile strength value of the high-temperature alloy GH141 material obtained by the process method is improved by 45MPa, and the index is improved by 5%; compared with the standard material process, the yield strength value is improved by 60MPa, and the yield strength index is improved by 10.6%.
TABLE 2 GH141 Material Performance data by Standard Process and treatment of example 2
Figure BDA0002743650360000061
The GH141 alloy is a precipitation hardening type nickel-based wrought superalloy, and the structure after heat treatment is composed of gamma and gamma' [ Ni ]3(AlTi)]σ, μ and carbides (MC, M)6C、M23C6) See fig. 1GH141 alloy equilibrium phase diagram for composition. Referring to FIG. 2, FIG. 2 is an SEM image of a forging substrate after annealing and solution treatment, as can be seen from FIG. 2(a), the fine γ' of intragranular dispersion is coherent with the substrate γ, as can be seen from FIG. 2(b), the MC of grain boundary precipitation sheet shape is relatively large in size, and M is relatively large6C and M23C6Less carbide (MC + M) at 1100 deg.C or above6C) The dissolution is started, the amount is rapidly reduced, the gamma' in dispersion distribution is dissolved, and the carbide in the grain boundary is partially dissolved, so that the pinning effect on the grain boundary is reduced; then high temperature brazing treatment is carried out, the brazing temperature is between the aging temperature (900 ℃) and the solid solution temperature (1120 ℃), the temperature is slowly cooled to 800-900 ℃ after vacuum brazing, then the temperature is cooled to room temperature by argon, so that fine gamma' crystal grains grow up and are coherent with blocky gamma phases with a basal body having a non-eutectic lattice interface, the size of flaky MC is precipitated at the crystal boundary, and M is shown in figure 3(a)6C and M23C6The carbides are increased and are discontinuously precipitated in small particles along the grain boundary, as shown in fig. 3(b), the large-size flaky MC has an embrittling effect on the grain boundary, and the alloy plasticity is reduced; when the matrix is subjected to 900 ℃ standard process aging, the growth of the gamma' phase in the crystal is faster, and M is 870-900 DEG C23C6Precipitation peak temperature range for MC + M stable at aging temperature6C has little influence, see FIG. 4; the aging system of the invention is a three-stage method, the first stage is 830-8In the aging process at 60 ℃, the gamma ' phase is promoted to be gradually coarsened from the initial spherical particles into regularly arranged cubic morphology according to a step mechanism, so that the strengthening effect of the gamma ' phase which is dispersed and distributed on the alloy is facilitated, the influence of the aging temperature below 830 ℃ on the grain size is small, but the quantity and the size distribution of the main strengthening phase gamma ' particles and the low-temperature carbide phase in the alloy can be influenced, and the figure 5 shows that; the aging in the second and third temperature ranges is that Al and Ti elements are directionally diffused to form gamma' Ni3(AlTi)]In a better temperature range, a larger amount of gamma' phase is precipitated.
In conclusion, the process of the invention has less crystal boundary and intragranular carbide, less tendency of gamma 'phase growth, and fine gamma' improves the dislocation pinning crystal effect, and finally promotes the intragranular strength.
The above-mentioned contents are only for illustrating the technical idea of the present invention, and the protection scope of the present invention is not limited thereby, and any modification made on the basis of the technical idea of the present invention falls within the protection scope of the claims of the present invention.

Claims (6)

1. A process for improving yield strength of a GH141 material, comprising the steps of:
1) carrying out annealing treatment and solid solution treatment on the GH141 material according to a standard process to obtain a supplied matrix structure;
2) carrying out high-temperature brazing treatment on the supplied matrix structure obtained in the step 1) to obtain a matrix structure subjected to high-temperature brazing;
3) carrying out heat treatment on the matrix structure after high-temperature brazing obtained in the step 2), wherein the heat treatment conditions are as follows:
at 5.0X 10-2Heating to 830-860 ℃ below Pa air pressure, and keeping the temperature for 1-2 h;
then cooling the furnace to 710-730 ℃, and preserving heat for 8-9 h;
then cooling the furnace to 610-630 ℃, and preserving heat for 8-9 h;
then air cooling is carried out to below 80 ℃, and the heat treatment is completed.
2. The process for improving the yield strength of the GH141 material of claim 1, wherein the air cooling in step 3) is performed by:
argon gas was introduced with a blowing fan.
3. The process for improving the yield strength of the GH141 material of claim 1, wherein the supplied matrix structure obtained in step 1) is directly subjected to the heat treatment in step 3).
4. The process for improving the yield strength of the GH141 material of claim 1, wherein step 2) is:
and (2) carrying out argon arc welding on the supplied matrix structure obtained in the step 1) to obtain the matrix structure after argon arc welding.
5. The process for improving the yield strength of the GH141 material of claim 3 or 4, wherein the heat treatment conditions in step 3) are as follows:
at 4.0X 10-2Heating to 840 ℃ under the pressure of Pa, and preserving heat for 2 h;
then furnace cooling is carried out to 720 ℃, and heat preservation is carried out for 9 h;
then furnace cooling is carried out to 620 ℃, and heat preservation is carried out for 9 hours;
then argon is introduced and a blowing fan is used for cooling to 70 ℃.
6. The process for improving the yield strength of the GH141 material of claim 1, wherein the heat treatment conditions in step 3) are as follows:
at 3.0X 10-2Heating to 840 ℃ under Pa, and preserving heat for 1 h;
then furnace cooling is carried out to 710 ℃, and heat preservation is carried out for 8 hours;
then furnace cooling is carried out to 610 ℃, and heat preservation is carried out for 8 hours;
then argon is introduced, and a blowing fan is used for cooling to 60 ℃, so that the heat treatment is completed.
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CN113293344A (en) * 2021-06-04 2021-08-24 航天特种材料及工艺技术研究所 Brazing aging integrated treatment process for GH4099 nickel-based high-temperature alloy
CN113637928A (en) * 2021-07-16 2021-11-12 北京科技大学 High-temperature yield strength improving process of GH4738 alloy forge piece after vacuum brazing

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Publication number Priority date Publication date Assignee Title
CN113293344A (en) * 2021-06-04 2021-08-24 航天特种材料及工艺技术研究所 Brazing aging integrated treatment process for GH4099 nickel-based high-temperature alloy
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CN113637928A (en) * 2021-07-16 2021-11-12 北京科技大学 High-temperature yield strength improving process of GH4738 alloy forge piece after vacuum brazing

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