CN114540733A - Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries - Google Patents
Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries Download PDFInfo
- Publication number
- CN114540733A CN114540733A CN202210187831.9A CN202210187831A CN114540733A CN 114540733 A CN114540733 A CN 114540733A CN 202210187831 A CN202210187831 A CN 202210187831A CN 114540733 A CN114540733 A CN 114540733A
- Authority
- CN
- China
- Prior art keywords
- nickel
- based alloy
- temperature
- crystal
- alloy plate
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Withdrawn
Links
Images
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides a method for improving the high-temperature mechanical property of a nickel-based alloy by synergistically obtaining two types of special crystal boundaries, which adopts a deformation cold and hot control treatment method to cooperatively introduce a low sigma crystal boundary and a sawtooth crystal boundary, break the network connectivity of a straight random crystal boundary, increase the initiation and expansion resistance of the alloy along the crystal cracks and improve the high-temperature mechanical property of the alloy, and specifically comprises the following steps: the process route of high-temperature solution treatment → cold rolling deformation → high-temperature heat preservation treatment → controlled cooling treatment → low-temperature heat preservation treatment → water cooling. The invention synergistically obtains two types of special crystal boundaries on the premise of not changing alloy components, and has the advantages of simple process and easy realization; the proportion of low sigma crystal boundary of the nickel-based alloy treated by the method is more than or equal to 65 percent, wherein the proportion of sigma 3 crystal boundary is more than or equal to 60 percent; meanwhile, part of straight random crystal boundaries can be converted into sawtooth crystal boundaries, the average amplitude of the sawtooth crystal boundaries is ensured to be more than or equal to 0.6 mu m, and the room-temperature elongation of the alloy can still be ensured to be more than 50% after the alloy is in long-term service at high temperature.
Description
Technical Field
The invention belongs to the technical field of nickel-based alloys, and particularly relates to a method for improving high-temperature mechanical properties of a nickel-based alloy by synergistically obtaining two types of special crystal boundaries.
Background
With the increasing global warming problem, the high-temperature and high-pressure high-efficiency thermal power generation technology becomes more important, which also puts higher requirements on the high-temperature service performance of the material. The supercritical thermal power generation technology (a-USC) is a clean power generation technology with a wide application prospect, and has higher combustion efficiency and less carbon dioxide emission compared with the traditional power generation technology, so that more and more attention is paid to people. In the production process, the steam pressure of the ultra-supercritical thermal power generation technology is generally 30-35MPa, the steam temperature is generally 593-.
The Inconel617 alloy is a Cr-Mo-Co solid solution reinforced nickel-based high-temperature alloy, and is an important candidate material for high-temperature key components because the Inconel617 alloy can still keep good structure stability, excellent high-temperature strength, high-temperature oxidation resistance and high-temperature corrosion resistance under high-temperature and high-pressure conditions. However, research shows that in the long-term service process of the alloy, elements in the alloy diffuse to grain boundaries under the dual effects of stress and temperature, carbides are formed at the grain boundaries, the carbides weaken the fracture toughness of the grain boundaries, and voids are formed along the interface of the carbides and a matrix under the effect of the stress, so that crystal-following cracking finally occurs.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide a method for improving the high-temperature mechanical property of a nickel-based alloy by synergistically obtaining two types of special crystal boundaries.
In order to achieve the purpose, the design idea of the invention is as follows:
through adopting a deformation annealing and cooling speed control heat treatment (hereinafter referred to as deformation cold and heat control treatment) process, two types of special crystal boundaries are obtained in a synergistic manner to improve the high-temperature mechanical property of the nickel-based alloy, the low sigma proportion in the alloy is increased to more than 65%, wherein the sigma 3 crystal boundary proportion is increased to more than 60%, and carbide is inhibited from being precipitated in the crystal boundaries; converting the rest straight random crystal boundary into a sawtooth crystal boundary, wherein the average amplitude of the sawtooth crystal boundary is more than or equal to 0.6 mu m, and optimizing the distribution of carbide of the crystal boundary; meanwhile, a strong special crystal boundary network is formed, the connectivity of a straight random crystal boundary is broken, the crystal crack initiation and expansion resistance of the crystal boundary along the crystal crack are increased, and the high-temperature mechanical property of the nickel-based alloy is improved, and the method specifically comprises the following steps: the process route of high-temperature solution treatment → cold rolling deformation → high-temperature heat preservation treatment → cold and heat control treatment → low-temperature heat preservation treatment → water cooling. Solution treatment: 1100-; on the other hand, promote recrystallization and maintain proper grain size. Cold rolling deformation: 4-8% cold rolling deformation is adopted, and deformation energy is stored in grains through pre-deformation, so that preparation is provided for grain boundary migration in a high-temperature heat preservation process and improvement of low sigma grain boundary proportion. High-temperature heat preservation treatment: keeping the temperature at 1050 ℃ for 1-2h at 1000-; and in the heat preservation process, different types of crystal boundaries can be subjected to interactive decomposition, so that the connectivity of the straight random crystal boundaries is broken. And (3) cooling and heating control treatment: cooling to 650-750 ℃ at a cooling rate of 1-10 ℃/min; so that the element promotes the enrichment of part of the element in the grain boundary through vacancy-assisted diffusion during the cooling process. And (3) low-temperature heat preservation treatment: and (4) keeping the temperature for 1-4h at the end of controlled cooling, forming irregular carbide pinning crystal boundaries on the crystal boundaries, converting part of straight random crystal boundaries into saw-toothed random crystal boundaries, and optimizing the distribution of carbide on the crystal boundaries. Specifically, the method comprises the following steps: obviously, two types of special crystal boundaries are obtained through synergy, so that the precipitation of crystal boundary carbides is inhibited, the distribution of the crystal boundary carbides is changed, the initiation and expansion resistance along crystal cracks is improved, and the high-temperature mechanical property of the nickel-based alloy is expected to be improved.
A method for improving the high-temperature mechanical property of a nickel-based alloy by cooperatively obtaining two types of special crystal boundaries comprises the following steps of introducing the two types of special crystal boundaries (low sigma crystal boundaries and sawtooth crystal boundaries) by adopting a deformation cold and hot control treatment process:
(1) the nickel-based alloy plate is subjected to heat preservation for 0.5-2h at the temperature of 1100-;
(2) performing water quenching treatment on the nickel-based alloy plate subjected to heat preservation treatment in the step (1);
(3) carrying out 4-8% cold rolling deformation on the nickel-based alloy plate subjected to water quenching treatment in the step (2);
(4) the nickel-based alloy plate subjected to cold rolling deformation treatment in the step (3) is subjected to heat preservation for 1-2h at the temperature of 1000-;
(5) cooling the nickel-based alloy plate subjected to the heat preservation treatment in the step (4) to 650-750 ℃, and preserving heat for 1-4 h;
(6) preserving the heat of the nickel-based alloy plate subjected to the controlled cooling and heat preservation treatment in the step (5) for 1-4 hours, taking out and cooling to room temperature by water;
in the step (1), the nickel-based alloy plate comprises the following chemical components in percentage by weight: chromium (Cr): 20.0-24.0%, cobalt (Co): 10.0-15.0%, molybdenum (Mo): 8.0-10.0%, iron (Fe): less than or equal to 3.0%, manganese (Mn): less than or equal to 1.0%, silicon (Si): less than or equal to 1.0 percent, aluminum (Al): 0.8-1.5%, titanium (Ti): less than or equal to 0.6%, carbon (C): 0.05-0.15%, nickel (Ni): and (4) the balance.
As a preferred embodiment of the present invention, in the step (1), the thickness of the nickel-based alloy plate material is 3 to 6 mm.
In the step (1), the nickel-based alloy plate is made of Inconel617 as a preferred embodiment of the present invention.
As a preferred embodiment of the present invention, in the step (5), the cooling rate is 1 to 10 ℃/min.
In the step (5), the nickel-based alloy plate is subjected to a controlled cooling and heating treatment process to promote grain boundary segregation of molybdenum, chromium and carbon elements in the alloy during controlled cooling, and form a flat plate M at the grain boundary6C and M23C6。
As a preferred embodiment of the invention, a deformation cold and heat control treatment process is adopted, the proportion of the low sigma crystal boundary of the nickel-based alloy plate is more than or equal to 65 percent, wherein the proportion of the sigma 3 crystal boundary is more than or equal to 60 percent; the average amplitude of the processed sawtooth crystal boundary is more than or equal to 0.6 mu m.
Due to the adoption of the scheme, the invention has the beneficial effects that:
firstly, under the premise of not changing the components of the alloy, two types of special grain boundaries can be obtained in the alloy in a synergistic way only by a simple deformation cold and heat control treatment method, wherein the low sigma grain boundary proportion is more than or equal to 65 percent, the sigma 3 grain boundary proportion is more than or equal to 60 percent, and grain boundary carbide precipitation is inhibited; meanwhile, the average amplitude of the sawtooth crystal boundary is more than or equal to 0.6 mu m, and the distribution of carbide of the crystal boundary is optimized; obviously increases the initiation and expansion resistance of the alloy along crystal cracks, and effectively improves the high-temperature mechanical property of the nickel-based alloy.
Secondly, the nickel-based alloy plate treated by the method has better room-temperature mechanical property, the yield strength is more than 300MPa, the tensile strength is more than 680MPa, and the elongation is more than 60%.
Thirdly, after the nickel-based alloy plate treated by the method is in service at high temperature for a long time, the yield strength of the alloy at room temperature is more than 300MPa, the tensile strength is more than 680MPa, and the elongation is more than 55%.
Drawings
FIG. 1 is a graph showing the distribution results of grain boundary characteristics after conventional treatment and deformation and cooling-control heat treatment of an Inconel617 alloy of the present invention (wherein (a) is a conventionally treated alloy (which is not subjected to cold rolling deformation and cooling-control treatment), and (b) is a deformation and heating-control treated alloy).
Fig. 2 is an SEM result chart of the saw grain boundary of the Inconel617 alloy plate material in example 1 of the present invention.
Detailed Description
The invention provides a method for improving the high-temperature mechanical property of a nickel-based alloy by synergistically obtaining two types of special crystal boundaries.
The invention discloses a method for improving the high-temperature mechanical property of a nickel-based alloy by cooperatively obtaining two types of special crystal boundaries, which adopts a deformation cold-controlled heat treatment process to simultaneously introduce the two types of special crystal boundaries (low sigma crystal boundaries and sawtooth crystal boundaries), and specifically comprises the following steps:
(1) performing high-temperature heat preservation treatment on the nickel-based alloy plate, wherein the treatment method is that the heat is preserved for 0.5 to 2 hours (preferably 1 hour) at the temperature of 1100 ℃ and 1200 ℃ (preferably 1100 ℃);
(2) performing water quenching treatment on the nickel-based alloy plate subjected to heat preservation treatment in the step (1);
(3) performing cold rolling deformation on the nickel-based alloy plate subjected to water quenching treatment in the step (2), wherein the deformation is 4-8% (preferably 5%);
(4) the nickel-based alloy plate subjected to the cold rolling deformation treatment in the step (3) is subjected to heat preservation for 1-2h (preferably 1h) at 1050 ℃ of 1000-;
(5) cooling the nickel-based alloy plate subjected to the heat preservation treatment in the step (4) to 650-750 ℃ (preferably 700 ℃), and preserving heat for 1-4h (preferably 4 h);
(6) and (4) preserving the heat of the nickel-based alloy plate subjected to the controlled cooling and heat preservation treatment in the step (5) for 1-4h (preferably 4h), taking out and cooling to room temperature by water.
In the step (1), the nickel-based alloy plate is marked with Inconel617, and comprises the following chemical components in percentage by weight: cr: 20.0-24.0%, Co: 10.0-15.0%, Mo: 8.0-10.0%, Fe: less than or equal to 3.0 percent, Mn: less than or equal to 1.0 percent, Si: less than or equal to 1.0 percent, Al: 0.8-1.5%, Ti: less than or equal to 0.6 percent, C: 0.05-0.15%, Ni: and (4) the balance.
In step (1), the thickness of the nickel-base alloy plate material is 3-6mm (preferably 3 mm).
In step (5), the cooling rate is 1-10 deg.C/min (preferably 5 deg.C/min).
In the step (5), the nickel-based alloy plate adopts a cooling and heating control treatment process to promote Mo, Cr and C elements in the alloy to generate grain boundary segregation in the cooling control process, and form a flat-plate-shaped M at the grain boundary6C and M23C6The grain boundary migration is dragged, and a saw grain boundary is formed between grains.
By adopting a deformation cold and hot control treatment process, the proportion of low sigma crystal boundaries of the nickel-based alloy plate is enabled to be more than or equal to 65 percent, wherein the proportion of sigma 3 crystal boundaries is more than or equal to 60 percent, and the precipitation of crystal boundary carbides is inhibited; and simultaneously, a sawtooth crystal boundary is introduced, the average amplitude of the sawtooth crystal boundary is more than or equal to 0.6 mu m, and the distribution of carbide of the crystal boundary is optimized.
Two types of special crystal boundaries are obtained in the alloy in a synergistic way; compared with the introduction of a single type of special crystal boundary, the treatment further improves the proportion of the special crystal boundary, forms more special crystal boundary network structures, breaks the connectivity of a straight random crystal boundary, and increases the initiation and expansion resistance along crystal cracks.
The nickel-based alloy plate subjected to the deformation cold and heat control treatment process is subjected to heat preservation for 5-24 hours at the temperature of 700-. After the high-temperature heat preservation treatment, the room-temperature mechanical properties of the alloy are carried out according to GB/T228.1 part 1 room-temperature test method of metal material tensile test.
The technical content of the present invention will be further described with reference to examples. The following examples are illustrative and not intended to be limiting, and are not intended to limit the scope of the invention. The experimental procedures used in the following examples are all conventional procedures unless otherwise specified.
Example 1:
in this example, an Inconel617 alloy plate having a thickness of 3mm was subjected to deformation cooling and heating treatment, and the low sigma grain boundary ratio was 76%, the sigma 3 grain boundary ratio was 65%, and the average amplitude of the saw tooth grain boundaries was 0.65 μm. The specific implementation process comprises the following steps:
(1) and placing the Inconel617 alloy plate in a heat treatment furnace, preserving the heat at 1100 ℃ for 1h, and taking out for water quenching treatment.
(2) And (3) carrying out cold rolling deformation on the Inconel617 alloy plate subjected to water quenching treatment in the step (1) by 5% by using a four-roller cold rolling mill.
(3) And (3) carrying out high-temperature heat preservation treatment on the Inconel617 alloy plate subjected to cold rolling deformation treatment in the step (2), namely, carrying out heat preservation for 1h at 1050 ℃.
(4) And (4) cooling the Inconel617 alloy plate subjected to heat preservation treatment in the step (3) to 700 ℃ at a cooling speed of 5 ℃/min, and preserving heat for 4 h.
(5) And (4) insulating the Inconel617 alloy plate subjected to the controlled cooling and heat preservation treatment in the step (4) for 4 hours, taking out and cooling to room temperature by water.
(6) And (3) cutting a sample from the Inconel617 alloy plate treated in the step (5) and performing EBSD analysis. The results are shown in FIG. 1, with dark colors representing random grain boundaries. After deformation cold and heat control treatment, the proportion of low sigma grain boundaries in the alloy is increased to 76%, wherein the proportion of sigma 3 grain boundaries is increased to 65%, and the connectivity of random grain boundary grids is broken.
(7) And (3) cutting a sample from the Inconel617 alloy plate treated in the step (5), and performing SEM analysis to convert part of straight random grain boundaries in the alloy after the deformation cooling and heating control treatment into sawtooth grain boundaries (figure 2). Wherein the average amplitude of the saw-tooth grain boundaries was 0.64. mu.m.
(8) And (3) carrying out mechanical property test on the Inconel617 alloy plate treated in the step (5) by referring to GB/T228.1 part 1 room temperature test method for metal material tensile test, wherein the results are shown in Table 1.
(9) And (4) placing the Inconel617 alloy plate treated in the step (5) in a high-temperature furnace, and simulating high-temperature service conditions, namely, keeping the temperature at 900 ℃ of 700 ℃ and 900 ℃ for 5-24h (keeping the temperature at 900 ℃ for 10h in the embodiment).
(10) And (3) performing mechanical property test on the nickel-based Inconel617 alloy plate treated in the step (9) by referring to GB/T228.1 part 1 room temperature test method for metal material tensile test, wherein the results are shown in Table 2.
TABLE 1 mechanical Properties of Inconel617 alloy plate
TABLE 2 Inconel617 alloy plate mechanical property after high-temperature service
In the Inconel617 alloy plate with the plate thickness of 3mm, after deformation cooling and heating control treatment, low sigma crystal boundaries and saw tooth crystal boundaries are introduced into the alloy at the same time, wherein the proportion of the low sigma crystal boundaries is 76%, the proportion of the sigma 3 crystal boundaries is 65%, part of straight random crystal boundaries are converted into the saw tooth crystal boundaries, and the average amplitude of the saw tooth crystal boundaries is 0.65 μm. The room temperature elongation of the alloy is more than or equal to 60 percent, and the room temperature elongation after high-temperature service is more than or equal to 55 percent.
Example 2:
the difference from the embodiment 1 is that the Inconel617 alloy plate used has the thickness of 4mm, the solid solution temperature of 1150 ℃ is kept for 2h, 6% pre-deformation is adopted, 1000 ℃ is kept for 2h, then the plate is cooled to 750 ℃ at the cooling speed of 1 ℃/min and kept for 1h, the plate is taken out and cooled to room temperature, the low sigma crystal boundary proportion in the alloy is 78%, the sigma 3 crystal boundary proportion reaches 66%, and the average amplitude of the sawtooth crystal boundary is 0.72 mu m.
A4 mm thick Inconel617 alloy plate having the same chemical composition as that of example 1 was subjected to deformation cooling and heating control treatment. Keeping the temperature at 1150 ℃ for 2h, and then carrying out water quenching treatment; after 6% cold rolling deformation, heat preservation treatment is carried out at 1000 ℃ for 2h, the steel is cooled to 750 ℃ at the cooling speed of 1 ℃/min and is preserved for 1h, and the steel is taken out and cooled to room temperature by water. The EBSD is adopted to carry out grain boundary structure analysis, and the result shows that the proportion of low sigma grain boundaries in the alloy reaches 78 percent, the proportion of sigma 3 grain boundaries in the alloy reaches 66 percent, the average amplitude of sawtooth grain boundaries is 0.72 mu m, and the connectivity of straight random grain boundaries is interrupted. The Inconel617 alloy plate is subjected to mechanical property test according to GB/T228.1 part 1 Room temperature test method for tensile test of metal materials, and the results are shown in Table 3. The treated plate is subjected to high-temperature heat preservation treatment (700 ℃ for 24 hours), and mechanical property tests are carried out according to GB/T228.1 part 1 room temperature test method of metal material tensile test, and the results are shown in Table 4.
TABLE 3 mechanical Properties of Inconel617 alloy plate
TABLE 4 mechanical properties of Inconel617 alloy plate after high-temperature service
In the Inconel617 alloy plate with the plate thickness of 4mm, after deformation cold and heat control treatment (6% deformation + heat preservation at 1000 ℃ for 2h +1 ℃/min to 750 ℃ for 1h + water cooling), a large amount of low sigma crystal boundaries appear in the alloy, the proportion reaches 78%, the proportion of sigma 3 crystal boundaries reaches 66%, meanwhile, part of straight random crystal boundaries are converted into sawtooth crystal boundaries, and the average amplitude of the sawtooth crystal boundaries is 0.72 mu m. The elongation at room temperature of the alloy is more than or equal to 60 percent, and the elongation at room temperature after high-temperature service is more than or equal to 55 percent.
Example 3:
the difference from the embodiment 1 is that the Inconel617 alloy plate used has the thickness of 5mm, the solid solution temperature of 1200 ℃ is kept for 0.5h, 8% pre-deformation is adopted, 1050 ℃ and 2h are kept, then the plate is cooled to 650 ℃ at the cooling speed of 8 ℃/min and kept for 4h, the plate is taken out and cooled to room temperature, the proportion of low sigma crystal boundary in the alloy is 74%, the proportion of sigma 3 crystal boundary reaches 64%, and the average amplitude of sawtooth crystal boundary is 0.68 μm.
A5 mm thick Inconel617 alloy plate having the same chemical composition as that of example 1 was subjected to deformation cooling and heating control treatment. Keeping the temperature at 1200 ℃ for 0.5h, and then carrying out water quenching treatment; after 8% cold rolling deformation, carrying out heat preservation treatment at 1050 ℃ for 2h, cooling to 650 ℃ at a cooling speed of 8 ℃/min, preserving heat for 4h, taking out, and cooling to room temperature by water. The EBSD is adopted to carry out grain boundary structure analysis, and the result shows that the proportion of sigma grain boundaries in the alloy reaches 74 percent, the proportion of sigma 3 grain boundaries in the alloy reaches 64 percent, the average amplitude of sawtooth grain boundaries is 0.68 mu m, and the connectivity of straight random grain boundaries is broken. The Inconel617 alloy plate was subjected to mechanical property testing according to GB/T228.1 part 1 Room temperature test method for tensile testing of metallic materials, and the results are shown in Table 5. The treated plate is subjected to high-temperature heat preservation treatment (800 ℃ for 12 hours), and mechanical property tests are carried out according to GB/T228.1 part 1 room temperature test method of metal material tensile test, and the results are shown in Table 6.
TABLE 5 mechanical Properties of Inconel617 alloy plate
TABLE 6 mechanical properties of Inconel617 alloy plate after high-temperature service
In the Inconel617 alloy plate with the plate thickness of 5mm, after deformation cold and heat control treatment (8% deformation +1050 ℃ heat preservation for 2h +8 ℃/min cooling to 650 ℃ heat preservation for 4h + water cooling), a large amount of low sigma crystal boundaries appear in the alloy, the proportion reaches 74%, the proportion of sigma 3 crystal boundaries reaches 64%, meanwhile, part of straight random crystal boundaries are converted into sawtooth crystal boundaries, the average amplitude of the sawtooth crystal boundaries is 0.68 mu m, the room temperature elongation of the alloy is more than or equal to 60%, and the room temperature elongation after high-temperature service is more than or equal to 55%.
In conclusion, the purpose of the invention can be realized within the process parameter range of the technical scheme of the invention. Two types of special crystal boundaries are obtained through deformation cold and heat control treatment, so that the high-temperature mechanical property of the alloy is obviously improved.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. It will be readily apparent to those skilled in the art that various modifications to these embodiments and the generic principles defined herein may be applied to other embodiments without the use of the inventive faculty. Therefore, the present invention is not limited to the above-described embodiments. Those skilled in the art should appreciate that many modifications and variations are possible in light of the above teaching without departing from the scope of the invention.
Claims (6)
1. A method for improving the high-temperature mechanical property of a nickel-based alloy by synergistically obtaining two types of special crystal boundaries is characterized by comprising the following steps of: the method adopts a deformation cold-controlled heat treatment process to introduce a low sigma crystal boundary and a sawtooth crystal boundary, and comprises the following steps:
(1) the nickel-based alloy plate is subjected to heat preservation for 0.5-2h at the temperature of 1100-;
(2) performing water quenching treatment on the nickel-based alloy plate subjected to heat preservation treatment in the step (1);
(3) carrying out 4-8% cold rolling deformation on the nickel-based alloy plate subjected to water quenching treatment in the step (2);
(4) the nickel-based alloy plate subjected to cold rolling deformation treatment in the step (3) is subjected to heat preservation for 1-2h at the temperature of 1000-;
(5) cooling the nickel-based alloy plate subjected to the heat preservation treatment in the step (4) to 650-750 ℃, and preserving heat for 1-4 h;
(6) preserving the heat of the nickel-based alloy plate subjected to the controlled cooling and heat preservation treatment in the step (5) for 1-4 hours, taking out and cooling to room temperature by water;
in the step (1), the nickel-based alloy plate comprises the following chemical components in percentage by weight: chromium: 20.0-24.0%, cobalt: 10.0-15.0%, molybdenum: 8.0-10.0%, iron: less than or equal to 3.0 percent, manganese: less than or equal to 1.0%, Si: less than or equal to 1.0 percent, aluminum: 0.8-1.5%, titanium: less than or equal to 0.6 percent, carbon: 0.05-0.15%, nickel: and (4) the balance.
2. The method for improving the high temperature mechanical property of the nickel-based alloy by synergistically obtaining two types of special grain boundaries according to claim 1, wherein: in the step (1), the thickness of the nickel-based alloy plate is 3-6 mm.
3. The method for improving the high temperature mechanical property of the nickel-based alloy by synergistically obtaining two types of special grain boundaries according to claim 1, wherein: in the step (1), the nickel-based alloy plate is under the trade name of Inconel 617.
4. The method for improving the high temperature mechanical property of the nickel-based alloy by synergistically obtaining two types of special grain boundaries according to claim 1, wherein: in the step (5), the cooling speed is 1-10 ℃/min.
5. The method for improving the high temperature mechanical property of the nickel-based alloy by synergistically obtaining two types of special grain boundaries according to claim 1, wherein: in the step (5), the nickel-based alloy plate adopts a cooling and heating control treatment process to promote the molybdenum, the chromium and the carbon elements in the alloy to generate grain boundary segregation in the cooling control process and form a flat-plate-shaped M at the grain boundary6C and M23C6Pinning crystal boundary, converting partial straight crystal boundary into sawtooth crystal boundary, and keeping temperature at low temperature is favorable for precipitation of carbide.
6. The method for improving the high temperature mechanical property of the nickel-based alloy by synergistically obtaining two types of special grain boundaries according to claim 1, wherein: by adopting a deformation cold and heat control treatment process, the proportion of the low sigma crystal boundary of the nickel-based alloy plate is more than or equal to 65 percent, wherein the proportion of the sigma 3 crystal boundary is more than or equal to 60 percent; the average amplitude of the treated sawtooth crystal boundary is more than or equal to 0.6 mu m.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210187831.9A CN114540733A (en) | 2022-02-28 | 2022-02-28 | Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210187831.9A CN114540733A (en) | 2022-02-28 | 2022-02-28 | Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN114540733A true CN114540733A (en) | 2022-05-27 |
Family
ID=81680438
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210187831.9A Withdrawn CN114540733A (en) | 2022-02-28 | 2022-02-28 | Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114540733A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115679230A (en) * | 2022-10-25 | 2023-02-03 | 重庆理工大学 | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy |
-
2022
- 2022-02-28 CN CN202210187831.9A patent/CN114540733A/en not_active Withdrawn
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115679230A (en) * | 2022-10-25 | 2023-02-03 | 重庆理工大学 | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy |
| CN115679230B (en) * | 2022-10-25 | 2024-01-05 | 重庆理工大学 | Surface treatment process for improving hydrogen embrittlement resistance of nickel-based corrosion-resistant alloy |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO2021121185A1 (en) | High-strength and high-toughness antioxidant iron-nickel-based high-temperature alloy, and preparation method thereof | |
| CN103993202B (en) | A kind of ultra supercritical station boiler tubing nickel-base alloy and preparation method | |
| CN104630597B (en) | A kind of iron nickel and chromium high temperature alloy and its manufacture method | |
| CN107557616B (en) | Nickel-based corrosion-resistant alloy pipe and manufacturing method thereof | |
| CN106957943B (en) | A kind of heat treatment method improving austenite heat-resistance steel mechanical property | |
| CN106086582B (en) | The technique for improving the low Σ coincidence lattice grain boundaries ratio of the Ni-based Incoloy925 alloys of iron | |
| CN111471897B (en) | Preparation and forming process of high-strength nickel-based high-temperature alloy | |
| CN114540732A (en) | Method for synergistically obtaining low sigma grain boundaries and saw-tooth grain boundaries | |
| CN105886841A (en) | Technology for increasing proportion of low sigma coincidence site lattice grain boundary of nickel-base superalloy Hastelloy N | |
| CN111411266B (en) | Preparation process of nickel-based high-tungsten polycrystalline superalloy | |
| CN109554629A (en) | A kind of ultra supercritical coal-fired unit steel and preparation method thereof | |
| CN110484836B (en) | Hafnium zirconium titanium molybdenum reinforced austenitic stainless steel and preparation method thereof | |
| CN114540733A (en) | Method for improving high-temperature mechanical property of nickel-based alloy by synergistically obtaining two types of special crystal boundaries | |
| CN110964995A (en) | Increase sigma 3 IN IN718 nickel-base superalloynMethod for proportion of type crystal boundary | |
| CN107058702A (en) | A kind of heat treatment method for improving room temperature impact flexibility after austenitic heat-resistance steel timeliness | |
| CN109898028B (en) | High-temperature oxidation resistant austenitic heat-resistant stainless steel and preparation method and application thereof | |
| CN113528979B (en) | High-strength RAFM steel with optimized components and heat treatment process thereof | |
| CN113604760B (en) | Method for improving strength stability of GH4738 alloy forging subjected to sub-solid solution treatment | |
| CN104674144A (en) | Heat treatment method of large-size, high-strength and fine-grain nickel-based superalloy forge piece for nuclear reactor | |
| CN110484702B (en) | Heat treatment method for realizing grain boundary sawtooth of iron-nickel-based alloy | |
| CN113957291B (en) | Rapid heat treatment method of high-strength nickel-based high-temperature alloy for power station | |
| CN111705195B (en) | Precipitation strengthening heat treatment process for Nb-containing austenitic heat-resistant steel | |
| US11739408B1 (en) | Heat treatment method for realizing grain boundary serration in nickel-based superalloy forging | |
| CN112025137A (en) | High-temperature corrosion-resistant nickel-based welding wire and smelting and preparation method thereof | |
| CN117802351B (en) | High-strength corrosion-resistant titanium alloy pipe and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| WW01 | Invention patent application withdrawn after publication | ||
| WW01 | Invention patent application withdrawn after publication |
Application publication date: 20220527 |