CN116837309A - Heat treatment method for reducing segregation of GH2984 niobate of superalloy - Google Patents
Heat treatment method for reducing segregation of GH2984 niobate of superalloy Download PDFInfo
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- 238000000034 method Methods 0.000 title claims abstract description 100
- 238000010438 heat treatment Methods 0.000 title claims abstract description 49
- 238000005204 segregation Methods 0.000 title claims abstract description 27
- 229910000601 superalloy Inorganic materials 0.000 title claims description 9
- 239000000956 alloy Substances 0.000 claims abstract description 117
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 114
- 238000000265 homogenisation Methods 0.000 claims abstract description 78
- 239000000463 material Substances 0.000 claims abstract description 60
- 230000008569 process Effects 0.000 claims abstract description 54
- 238000005242 forging Methods 0.000 claims abstract description 40
- 238000005096 rolling process Methods 0.000 claims abstract description 30
- 239000006104 solid solution Substances 0.000 claims abstract description 5
- 230000000630 rising effect Effects 0.000 claims abstract description 3
- 239000000243 solution Substances 0.000 claims description 26
- 238000004321 preservation Methods 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 10
- 150000002822 niobium compounds Chemical class 0.000 abstract description 56
- 238000009827 uniform distribution Methods 0.000 abstract description 9
- 239000010419 fine particle Substances 0.000 abstract 1
- 230000000149 penetrating effect Effects 0.000 description 18
- 230000007547 defect Effects 0.000 description 13
- 239000000203 mixture Substances 0.000 description 10
- 239000000126 substance Substances 0.000 description 10
- 238000003723 Smelting Methods 0.000 description 9
- 238000010586 diagram Methods 0.000 description 9
- 238000004512 die casting Methods 0.000 description 9
- 238000004220 aggregation Methods 0.000 description 8
- 230000002776 aggregation Effects 0.000 description 8
- 238000009826 distribution Methods 0.000 description 8
- 238000005336 cracking Methods 0.000 description 4
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 210000001787 dendrite Anatomy 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000002045 lasting effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229910000484 niobium oxide Inorganic materials 0.000 description 1
- URLJKFSTXLNXLG-UHFFFAOYSA-N niobium(5+);oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[O-2].[O-2].[Nb+5].[Nb+5] URLJKFSTXLNXLG-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
Classifications
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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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
- B21B1/026—Rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Forging (AREA)
Abstract
The invention discloses a heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate, which comprises the procedures of ingot cogging, cogging square three-section homogenization and total solid solution treatment of materials after forging/rolling; and the temperature rising speed of the primary homogenization and the secondary homogenization of the cogging square is 100-150 ℃/h. The method can effectively reduce the segregation degree of the niobium compound of the high-temperature alloy GH2984, and the niobium compound of the metallographic structure of the material has fine particles and uniform distribution and is not easy to crack in the deep processing process.
Description
Technical Field
The invention belongs to the technical field of heat treatment of metal materials, and particularly relates to a heat treatment method for reducing segregation of GH2984 niobate of a superalloy.
Background
GH2984 is Fe-Ni-Cr based precipitation strengthening type deformation superalloy, and the main products are bars and pipes. The working temperature of the bar and the deep processing pipe thereof is 700-750 ℃, the alloy is subjected to solid solution strengthening by elements such as chromium, molybdenum, niobium and the like, and forms a precipitation strengthening phase by a small amount of aluminum and titanium elements, and the alloy has good long-term lasting strength, oxidation resistance and corrosion resistance, good cold and hot processing performance, better tissue stability and welding performance. Compared with high-temperature alloy with the same kind of application, the alloy can save w (Ni) by 33 percent and has larger cost advantage. After long-term aging, a small amount of granular phase a is separated out, and the performance is not affected. The alloy has no intergranular corrosion phenomenon in various heat treatment states and welding.
The alloy heat pipe belongs to a short-flow and high-efficiency metal material deformation process technology, and is a main production process of a seamless alloy pipe. The tube blank is extruded and rubbed during the tube penetrating deformation process, the temperature of the tube blank is rapidly increased, and the segregation phenomenon of the low-melting-point niobium compound with different degrees is commonly existed in the high-temperature alloy material, so that the tube blank is cracked due to the local melting phenomenon in the alloy tube blank material. Through the technological means, the niobium compound in the high-temperature alloy is decomposed and diffused, the segregation degree of the niobium compound is greatly reduced, the problem of deformation and cracking of the high-temperature alloy penetrating pipe is effectively solved, and the method has great significance in improving the quality of alloy pipe products.
Disclosure of Invention
The invention aims to provide a heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate, which can effectively solve the cracking problem of high-temperature alloy GH2984 in the subsequent deep processing process.
In order to solve the technical problems, the invention adopts the following technical scheme:
a heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate comprises three steps of ingot cogging, cogging square homogenization and material complete solid solution treatment after forging/rolling; and the temperature rising speed of the primary homogenization and the secondary homogenization of the cogging square is 100-150 ℃/h.
In the ingot cogging process, cogging is carried out on a high-temperature alloy GH2984 ingot obtained through smelting, die casting and remelting, and cogging deformation is more than or equal to 1.4, so that a high-temperature alloy GH2984 cogging method is obtained.
The invention relates to a three-section homogenizing procedure of a cogging square, wherein the specific operation of one-section homogenizing treatment is as follows: raising the temperature of the high-temperature alloy GH2984 cogging square to 700-800 ℃ at the speed of 100-150 ℃/h, and preserving the heat for 1-2 h.
The invention relates to a three-section homogenizing procedure of a cogging square, wherein the specific operation of the two-section homogenizing treatment is as follows: after the homogenization of the first section is finished, the temperature of the high-temperature alloy GH2984 cogging is raised to 1150-1200 ℃ along with the furnace at the speed of 100-150 ℃/h, and the temperature is kept for 10-15 h.
The invention relates to a three-section homogenizing procedure of a cogging square, wherein the specific operation of the three-section homogenizing treatment is as follows: cooling the high-temperature alloy GH2984 cogging square to 1090-1140 ℃ along with the furnace after the second-stage homogenization is finished, preserving heat for 2-4 h, and starting forging/rolling after the heat preservation is finished.
The invention relates to a process for carrying out complete solid solution treatment on a forged/rolled material, which is characterized in that the high-temperature alloy GH2984 is kept at 1050-1150 ℃ for 1-2 h.
The metallographic structure niobium oxide particles of the high-temperature alloy GH2984 obtained by the method are fine and uniformly distributed, and are not easy to crack in the deep processing process.
The design idea of the invention is as follows:
the invention precisely controls the heating rate of the high-temperature alloy GH2984 in the heat treatment process, and controls the heating rate to be 100-150 ℃/h. The heating rate is too low, the grain structure growth speed is higher, and the carbide precipitation amount is increased, so that the plasticity and toughness of the material are reduced; the heating rate is too high, and the nickel-based alloy material has poor heat conductivity, generates larger thermal stress, is easy to generate heating defects and even causes the cracking of the cogging square.
And fully breaking ingot dendrites in the cogging process, and greatly eliminating the segregation defect of the niobium compound in the as-cast structure. According to thermodynamic conditions, the cogging formula is kept at a constant temperature in a high-temperature interval to enable atoms to accumulate enough energy to break through an energy barrier, so that the niobate bonding bonds are broken, fine niobate particles are uniformly distributed on an alloy matrix, the defect of segregation of an as-cast structure of the steel ingot is effectively weakened, and the purpose of reducing the segregation of the niobate is achieved.
The beneficial effects of adopting above-mentioned technical scheme to produce lie in: 1. the invention controls the cogging deformation of GH2984 high-temperature alloy cast ingot to be not less than 1.4, so that the niobium compound segregation defect in the cast structure is fully decomposed along with the breaking of dendrite. 2. The invention controls the heating rate of the GH2984 high-temperature alloy in the heat treatment process to be 100-150 ℃/h, reduces the heating defect of the material, keeps the original plasticity of the material and does not reduce the yield of the product. 3. The invention has clear requirements on heating speed, heat preservation interval and heat preservation time, improves the decomposition efficiency of niobium compounds in the homogenizing process of the material, and can obviously improve the mechanical properties of the alloy material. 4. The method can effectively solve the problem of deformation and cracking of the high-temperature alloy GH2984 in the subsequent deep processing process.
Drawings
FIG. 1 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 1;
FIG. 2 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 2;
FIG. 3 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 3;
FIG. 4 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 4;
FIG. 5 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 5;
FIG. 6 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 6;
FIG. 7 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 7;
FIG. 8 is a metallographic structure diagram of GH2984 material after heat treatment by the method of example 8;
FIG. 9 is a metallographic structure diagram of GH2984 material without heat treatment by the method.
Description of the embodiments
The present invention will be described in further detail with reference to specific examples.
Example 1
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.4, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 700 ℃ at the speed of 100 ℃/h, and preserving heat for 1h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is increased to 1150 ℃ along with a furnace at the speed of 120 ℃/h, and the temperature is kept for 12h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1140 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 3.5h, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the high temperature alloy GH2984 is kept at 1000 ℃ for 1.5h.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 1, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 1 and the graph 9, but the size of the granular niobium compounds in the graph 1 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 2
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.4, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 800 ℃ at the speed of 100 ℃/h, and preserving heat for 1.5h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1180 ℃ along with a furnace at the speed of 100 ℃/h, and the temperature is kept for 10h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1140 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 3 hours, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the high temperature alloy GH2984 is kept at 1100 ℃ for 1h.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 2, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 2 and the graph 9, but the size of the granular niobium compounds in the graph 2 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 3
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.6, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 750 ℃ at the speed of 110 ℃/h, and preserving heat for 1h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1200 ℃ along with a furnace at the speed of 150 ℃/h, and the temperature is kept for 11h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1120 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 3 hours, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling the superalloy GH2984 was incubated for 2h at 1050 ℃.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 3, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 3 and the graph 9, but the size of the granular niobium compounds in the graph 3 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 4
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.4, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 700 ℃ at the speed of 130 ℃/h, and preserving heat for 2h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1190 ℃ along with a furnace at the speed of 150 ℃/h, and the temperature is kept for 12h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1100 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 4 hours, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the superalloy GH2984 is kept at 1150 ℃ for 1h.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 4, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 4 and the graph 9, but the size of the granular niobium compounds in the graph 4 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 5
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.5, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 800 ℃ at the speed of 100 ℃/h, and preserving heat for 1.5h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1200 ℃ along with a furnace at the speed of 150 ℃/h, and the temperature is kept for 11h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1140 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 3 hours, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the superalloy GH2984 is kept at 1150 ℃ for 1h.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 5, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 5 and the graph 9, but the size of the granular niobium compounds in the graph 5 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 6
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.4, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 700 ℃ at the speed of 150 ℃/h, and preserving heat for 2h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1150 ℃ along with a furnace at the speed of 150 ℃/h, and the temperature is kept for 15h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1100 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 4 hours, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the high temperature alloy GH2984 is kept at 1100 ℃ for 1.5h.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 6, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 6 and the graph 9, but the size of the granular niobium compounds in the graph 6 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 7
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.4, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 800 ℃ at the speed of 100 ℃/h, and preserving heat for 1h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1180 ℃ along with a furnace at the speed of 150 ℃/h, and the temperature is kept for 12h; three-stage homogenization treatment: cooling the high-temperature alloy GH2984 cogging square to 1090 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 2.5h, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the high temperature alloy GH2984 is kept at 1100 ℃ for 1.5h.
The high-temperature alloy GH2984 material has the ingot specification phi 300mm and the forging rod specification phi 75mm, and the chemical composition and the mass percentage content are shown in table 1.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 7, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 7 and the graph 9, but the size of the granular niobium compounds in the graph 7 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
Example 8
The heat treatment method of the high-temperature alloy GH2984 comprises the following steps of ingot cogging, cogging square three-stage homogenization, and material complete solution treatment after forging/rolling:
(1) Ingot cogging process: cogging a high-temperature alloy GH2984 cast ingot obtained through smelting, die casting and remelting, wherein cogging deformation is 1.4, and a high-temperature alloy GH2984 cogging square is obtained;
(2) Three-stage homogenization treatment process of cogging side: and (3) carrying out a stage of homogenization treatment: raising the temperature of a high-temperature alloy GH2984 cogging square to 800 ℃ at the speed of 100 ℃/h, and preserving heat for 1.5h; two-stage homogenization treatment: after the homogenization of the first section is finished, the temperature of a high-temperature alloy GH2984 cogging square is raised to 1180 ℃ along with a furnace at the speed of 150 ℃/h, and the temperature is kept for 10h; three-stage homogenization treatment: cooling a high-temperature alloy GH2984 cogging square to 1100 ℃ along with a furnace after the second-stage homogenization is finished, preserving heat for 3 hours, and starting forging/rolling after the heat preservation is finished;
(3) Full solution treatment process: after forging/rolling, the high temperature alloy GH2984 is kept at 1100 ℃ for 1h.
The high-temperature alloy GH2984 material of the embodiment has the ingot specification phi of 300mm, the forging rod specification phi of 75mm, the chemical composition and the mass percentage of the forging rod are shown in the table 1, and the chemical composition and the mass percentage of the forging rod are shown as '9' in the table in fig. 9.
The metallographic structure of the high-temperature alloy GH2984 material treated by the method is shown in figure 8, and the structure of the high-temperature alloy GH2984 material which is not subjected to homogenization and solution treatment is shown in figure 9; as can be seen from the graph, the segregation conditions of the granular niobium compounds are shown in the graph 8 and the graph 9, but the size of the granular niobium compounds in the graph 8 is obviously reduced, the distribution is more uniform, the niobium compounds with small size and uniform distribution are not easy to generate heating defects in the subsequent deep processing deformation process of pipe penetrating and the like, and the granular niobium compounds have more stable mechanical properties; in fig. 9, the granular niobium compound has a larger size and forms an aggregation state, so that the granular niobium compound is easy to be locally melted in the subsequent deep processing deformation process of a penetrating pipe and the like, and the material is cracked.
TABLE 1 examples 1-8 superalloy GH2984 chemical composition (%)
The balance of the components in Table 1 are unavoidable impurities.
The above embodiments are only for illustrating the technical solution of the present invention, and it should be understood by those skilled in the art that although the present invention has been described in detail with reference to the above embodiments: modifications and equivalents may be made thereto without departing from the spirit and scope of the invention, which is intended to be encompassed by the claims.
Claims (6)
1. A heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate is characterized by comprising three steps of ingot cogging, cogging square homogenization and total solid solution treatment of materials after forging/rolling; and the temperature rising speed of the primary homogenization and the secondary homogenization of the cogging square is 100-150 ℃/h.
2. The heat treatment method for reducing segregation of GH2984 niobate, which is a superalloy, according to claim 1, wherein the deformation amount is not less than 1.4.
3. The heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate according to claim 1, wherein the three-stage cogging Fang Junzhi step comprises the following specific operations: raising the temperature of the high-temperature alloy GH2984 cogging square to 700-800 ℃ at the speed of 100-150 ℃/h, and preserving the heat for 1-2 h.
4. The heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate according to claim 1, wherein the three-stage cogging Fang Junzhi step comprises the following specific operations: after the homogenization of the first section is finished, the temperature of the high-temperature alloy GH2984 cogging is raised to 1150-1200 ℃ along with the furnace at the speed of 100-150 ℃/h, and the temperature is kept for 10-15 h.
5. The heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate according to claim 1, wherein the cogging-square three-stage homogenization process comprises the following specific operations: cooling the high-temperature alloy GH2984 cogging square to 1090-1140 ℃ along with the furnace after the second-stage homogenization is finished, preserving heat for 2-4 h, and starting forging/rolling after the heat preservation is finished.
6. The heat treatment method for reducing segregation of high-temperature alloy GH2984 niobate according to claim 1, wherein the total solution treatment process is characterized in that the high-temperature alloy GH2984 material is kept at 1050-1150 ℃ for 1-2 h after forging/rolling.
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