CN112813369A - High-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and preparation process thereof - Google Patents
High-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and preparation process thereof Download PDFInfo
- Publication number
- CN112813369A CN112813369A CN202011638416.8A CN202011638416A CN112813369A CN 112813369 A CN112813369 A CN 112813369A CN 202011638416 A CN202011638416 A CN 202011638416A CN 112813369 A CN112813369 A CN 112813369A
- Authority
- CN
- China
- Prior art keywords
- strip
- preparation process
- blank
- cold rolling
- plasticity
- 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.)
- Granted
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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The application relates to the technical field of nickel-based superalloy preparation processes, and particularly discloses a high-strength high-elasticity high-plasticity nickel-based superalloy strip and a preparation process thereof. The preparation process comprises the following steps: preparing a strip blank; primary cold rolling: carrying out primary cold rolling on the strip blank; water cooling and annealing: carrying out water-cooling annealing on the strip blank subjected to the primary cold rolling; secondary cold rolling: carrying out secondary cold rolling on the strip blank subjected to water-cooling annealing; and (3) continuous annealing: carrying out continuous annealing treatment on the strip blank subjected to the secondary cold rolling; and (3) cold rolling for three times: and carrying out three times of cold rolling on the strip blank after the continuous annealing to obtain a finished product strip. The nickel-based high-temperature alloy strip prepared by the preparation process has the advantages of excellent grain size, good matching of the number of gamma' strengthening phases, uniform and good structural properties, high strength and high plasticity; the preparation process is simple and has obvious popularization and application values.
Description
Technical Field
The application relates to the technical field of a nickel-based superalloy preparation process, in particular to a high-strength high-elasticity high-plasticity nickel-based superalloy strip and a preparation process thereof.
Background
The high-strength high-elasticity high-plasticity nickel-based high-temperature alloy is divided into solid solution strengthening type high-temperature alloy and precipitation hardening type high-temperature alloy according to a strengthening mode, a large amount of Al, Ti and other elements are added into the precipitation hardening type high-temperature alloy to form a gamma' aging strengthening phase, W, Co and other elements are added to perform solid solution strengthening, and B, Ce, Mg and other elements are added to perform grain boundary strengthening.
When the high-strength high-elasticity high-plasticity nickel-based precipitation hardening type high-temperature alloy strip is used for manufacturing certain special elastic components such as coil springs, the alloy strip is required to have high plasticity so as to meet the molding requirement, and the alloy strip is required to have high strength so as to meet the requirement on the rebound performance of the molded components. However, in the related art, annealing treatment is performed on the strip before cold rolling of the alloy finished strip by using the traditional process, so that good matching between the grain size of the strip and the number of gamma' strengthening phases cannot be obtained, and the finished strip cannot have high strength and high plasticity, has poor performance uniformity and unstable quality, and is difficult to meet the requirements of member forming and service performance at the same time.
Disclosure of Invention
In order to overcome the defects that a high-strength, high-elasticity and high-plasticity nickel-based high-temperature alloy strip cannot have high strength and high plasticity at the same time and has poor performance uniformity, the application provides a high-strength, high-elasticity and high-plasticity nickel-based high-temperature alloy strip and a preparation process thereof.
The application provides a high-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and a preparation process thereof, which adopt the following technical scheme:
a preparation process of a high-strength high-elasticity high-plasticity nickel-based superalloy strip comprises the following steps:
preparing a strip blank: smelting an alloy cast ingot, homogenizing the cast ingot, forging and cogging the homogenized cast ingot to obtain a plate blank, carrying out multi-fire hot rolling on the plate blank, and carrying out solid solution treatment on the hot-rolled plate blank;
primary cold rolling: mechanically polishing the plate blank subjected to the solution treatment and performing edge linear cutting to obtain a strip blank required by primary cold rolling, and performing primary cold rolling on the strip blank;
water cooling and annealing: carrying out water-cooling annealing on the strip blank subjected to the primary cold rolling;
secondary cold rolling: carrying out secondary cold rolling on the strip blank subjected to water-cooling annealing;
and (3) continuous annealing: carrying out continuous annealing treatment on the strip blank subjected to the secondary cold rolling;
the process parameters of continuous annealing are as follows: the continuous annealing temperature is 1050-1160 ℃, when the thickness of the finished product strip blank before cold rolling is 1.8-2.5 mm, the strip moving speed is 0.8-1.3 m/min; when the thickness of the belt blank is 1.6-1.8 mm, the belt conveying speed is 1.3-2.0 m/min; when the thickness of the strip blank is 1.3-1.6 mm, the speed of the strip is 2.0-2.5 m/min.
By adopting the technical scheme, the alloy ingot casting is smelted by adopting a mode of vacuum induction and electroslag remelting or vacuum induction and vacuum consumable remelting duplex ingot casting, compared with the mode of single ingot casting smelting, the components of the ingot casting are more uniform by the duplex ingot casting, and the impurity element removing effect is better;
the nickel-based high-temperature alloy strip prepared by the preparation process has a microstructure with the grain size well matched with the quantity of gamma' strengthening phases, so that the uniformity of the structure and the performance of the strip is ensured, and further, the finished strip has high strength and high plasticity and meets the requirements of the forming and the using performance of an elastic component;
by adopting a continuous annealing treatment process and optimizing the annealing temperature and the tape-moving speed in the continuous heat-preservation annealing process of the inert gas, the obtained finished product strip has smooth and clean surface, good straightness, high flattening efficiency and good quality; meanwhile, the structural property uniformity of the finished strip is obviously improved, the comprehensive mechanical property is improved, the nickel-based high-temperature alloy strip with high strength and high plasticity is obtained, and finally the forming and using performance of the elastic component can be met;
meanwhile, the preparation process is simple to operate, short in required time, high in production efficiency, capable of realizing large-scale industrial production, wide in industrial prospect and suitable for popularization and application.
Preferably, in the water-cooling annealing treatment, the annealing temperature is 1070 to 1170 ℃, the heat preservation time is calculated according to a formula of t ═ 2 to 4) d/min (d is the thickness of the blank), and air cooling or water cooling is adopted after annealing.
By adopting the technical scheme, the proper annealing temperature is selected to carry out annealing treatment on the strip blank, and the proper cooling mode is selected to cool the annealed strip blank after the annealing treatment, so that the hardness is reduced, the softening of the strip blank after cooling is ensured, and the work hardening is reduced; meanwhile, the residual stress can be reduced, and the deformation and cracking tendency of the strip blank can be reduced.
Preferably, the cold rolling deformation of the strip is 30-45%.
Preferably, the final cold deformation of the finished strip is 7-25%.
Preferably, the temperature of the solid solution treatment is 1050-1150 ℃, the heat preservation time is 20-60 min, and the cooling mode after the solid solution treatment adopts water cooling.
By adopting the technical scheme, the alloy is subjected to solution treatment at a proper temperature and for a proper heat preservation time, so that the gamma' strengthening phase is completely dissolved into the gamma matrix, and the alloy elements are not precipitated or subjected to phase change through rapid cooling, so that a strip blank obtains a good softening effect.
Preferably, the homogenization treatment temperature of the alloy ingot is 1160-1190 ℃, and the heat preservation time is calculated according to a formula of t ═ 13-20 d min/mm (d is the diameter of the alloy ingot).
By adopting the technical scheme, the alloy ingot is subjected to homogenization treatment, so that the distribution of alloy elements in the alloy ingot is more uniform, and the stress existing in the alloy ingot can be eliminated.
Preferably, the hot rolling heating temperature is 1100-1200 ℃, the primary heating heat preservation time is 1-3 h, and the subsequent hot rolling heating heat preservation time is calculated according to the thickness of the blank and a formula of t ═ 1.5-3.0) d/min (d is the thickness of the blank).
By adopting the technical scheme, the slab is subjected to hot rolling treatment at a proper hot rolling temperature and a proper heat preservation time, and heat preservation treatment is performed at the hot rolling temperature and the heat preservation time, so that the gamma 'strengthening phase in the alloy after hot rolling is fully precipitated, the quantity and the distribution of the gamma' strengthening phase are well matched, and the obtained finished product strip has high strength and high plasticity.
Preferably, the hot rolling deformation is 15-25%, and each hot rolling pass is 1-2.
By adopting the technical scheme, the alloy is subjected to hot rolling treatment by adopting a hot rolling mode with multiple fire times, so that on one hand, the alloy is uniformly heated; on the other hand, the cracking tendency of the alloy in the hot rolling process can be reduced, the cracking of the alloy in the hot rolling process can be reduced, the resource waste can be reduced, the cost can be saved, and the yield can be improved.
In summary, the present application has the following beneficial effects:
1. by optimizing the annealing temperature and the strip speed in the continuous protection annealing process of the inert gas and controlling the final cold rolling deformation, the finished strip has good matching of the grain size and the quantity of the gamma' strengthening phases, and the uniformity of the structure performance is obviously improved.
2. The belt material prepared by the method has the advantages of high surface quality, high strength and plasticity, uniform structure and excellent performance.
3. The preparation method has the advantages of energy conservation, high efficiency, simple process, short time, high popularization value, capability of realizing large-scale industrial production, high production efficiency, great improvement on resource utilization rate, wide industrial prospect and suitability for popularization and application.
Drawings
Fig. 1 is a photograph of the grain structure of the finished strip of example 1 of the present application.
Fig. 2 is a photograph of the reinforcing phase morphology of the finished strip γ' of example 1 of the present application.
Detailed Description
The present application will be described in further detail with reference to the following drawings and examples.
Homogenizing the alloy ingot: homogenizing the alloy cast ingot, wherein the temperature is 1100-1200 ℃, and the heat preservation time is calculated according to a formula that t is (13-20) dmin/mm (d is the diameter of the alloy cast ingot).
In this application, the homogenization temperature is typically, but not limited to, 1100 deg.C, 1110 deg.C, 1120 deg.C, 1130 deg.C, 1140 deg.C, 1150 deg.C, 1160 deg.C, 1170 deg.C, 1180 deg.C, 1190 deg.C, or 1200 deg.C.
In a preferred embodiment, the homogenization treatment temperature is 1100-1200 ℃, and when the homogenization treatment is in the above range, the alloy ingot is subjected to homogenization treatment, so that the element distribution in the alloy is more uniform, the obtained alloy ingot has more uniform components and more uniform structure, the residual stress of the alloy can be eliminated, and the cracking tendency of the alloy ingot is reduced.
The hot rolling heating temperature is 1100-1200 ℃, the primary heating heat preservation time is 2-3h, the subsequent hot rolling heating heat preservation time is calculated according to the thickness of the blank and a formula that t is (1.5-3.0) d/min (d is the thickness of the blank), the deformation in the hot rolling process is 15-25%, and the hot rolling pass of each fire is 1-2.
In the present application, the hot rolling heating temperature is typically, but not limited to, 1100 ℃, 1110 ℃, 1120 ℃, 1130 ℃, 1140 ℃, 1150 ℃, 1160 ℃, 1170 ℃, 1180 ℃, 1190 ℃ or 1200 ℃.
The initial heat soak time is typically, but not limited to, 2 hours, 2.5 hours, or 3 hours.
The amount of hot rolling distortion is typically, but not limited to, 15%, 15.5%, 16%, 16.5%, 17%, 17.5%, 18%, 18.5%, 19%, 19.5%, 20%, 20.5%, 21%, 21.5%, 22%, 22.5%, 23%, 23.5%, 24%, 24.5%, or 25%.
Each hot rolling pass is typically, but not limited to, 1 or 2 passes.
In any preferred embodiment, the temperature is maintained for 2-3h within the range of 1100-1200 ℃, and then hot rolling treatment is carried out, so that gamma 'strengthening phases in the alloy are fully precipitated, the number and distribution of the gamma' strengthening phases are well matched, and the obtained finished strip has high strength and high plasticity; when the temperature is too high or too low, the precipitation of the gamma 'strengthening phase in the alloy is insufficient, or the size of the gamma' strengthening phase is too large, so that the structural uniformity of the slab is poor, and the deformation of the slab in the hot rolling process is influenced.
When the hot rolling deformation of the slab is within the above priority range, the obtained slab has better structural uniformity and higher mechanical properties.
In the hot rolling process, the thickness of the plate blank is reduced along with the hot rolling process, and a proper hot rolling pass is selected to reduce the cracking tendency of the plate blank in the hot rolling process.
Examples
Example 1
In the embodiment, GH4578 alloy is used as a raw material.
The preparation process of the high-strength, high-elasticity and high-plasticity nickel-based superalloy strip provided by the embodiment comprises the following steps: preparing a strip blank:
smelting an alloy ingot: remelting by adopting vacuum induction and electric slag to complete alloy ingot smelting to obtain an electric slag ingot with the diameter of 120 mm; homogenizing: homogenizing the alloy cast ingot, wherein the homogenizing time is 1180 ℃ and the time is 40h, and performing primary mechanical polishing on the homogenized alloy cast ingot;
forging and cogging: forging and cogging the cast ingot subjected to primary mechanical grinding, and performing secondary mechanical grinding and primary edge linear cutting on the slab subjected to forging and cogging to obtain a slab required by hot rolling, wherein the thickness of the slab is 40 mm;
multiple-fire hot rolling of the plate blank: carrying out primary heating on a plate blank with the thickness of 40mm, wherein the heating temperature is 1150 ℃, the heat preservation time is 2.5h, carrying out hot rolling in two passes, the hot rolling deformation is 25%, and rolling to a plate blank with the thickness of 30 mm; after the furnace is returned and the temperature is kept for 70min, carrying out hot rolling for the second fire time, and carrying out hot rolling in two passes, wherein the hot rolling deformation is 25 percent, and the plate blank with the thickness of 22.5mm is obtained; after the furnace is returned and the temperature is kept for 50min, carrying out third hot rolling in two passes, wherein the hot rolling deformation is 24%, and the plate blank with the thickness of 17mm is rolled; after the furnace is returned and the temperature is kept for 40min, performing hot rolling for the fourth time, and performing hot rolling in two passes, wherein the hot rolling deformation is 25 percent, and the plate blank with the thickness of 12.8mm is obtained by rolling; after the furnace is returned and the temperature is kept for 30min, performing hot rolling for the fifth time, and performing hot rolling in two passes, wherein the hot rolling deformation is 25 percent, and the plate blank with the thickness of 9.6mm is obtained by rolling; hot rolling for the first five times, and hot rolling the blank with heat preservation cotton after discharging; after the furnace is returned and the temperature is kept for 20min, carrying out sixth hot rolling in a single pass, wherein the hot rolling deformation is 22%, and the plate blank with the thickness of 7.5mm is obtained; after the furnace is returned and the temperature is kept for 15min, carrying out seventh hot rolling in a single pass, wherein the hot rolling deformation is 23%, and rolling to a plate blank with the thickness of 5.8 mm; performing eighth hot rolling after the furnace is returned and the temperature is kept for 12min, performing single pass, wherein the hot rolling deformation is 23%, and rolling to a plate blank with the thickness of 4.5 mm;
plate blank solution treatment: carrying out solution treatment on the hot-rolled plate blank at the temperature of 1100 ℃ for 30min, and cooling by water cooling after the solution treatment;
primary cold rolling: mechanically polishing the plate blank subjected to the solution treatment and performing edge linear cutting to obtain a strip blank required by cold rolling; the deformation is 35 percent, and the strip is cold-rolled to a strip blank with the thickness of 2.7 mm;
water cooling and annealing: annealing the strip blank subjected to primary cold rolling, keeping the temperature at 1100 ℃ for 10min, then performing water cooling, and removing surface oxide skin by mechanical grinding;
secondary cold rolling: the deformation is 35 percent, and the strip is cold-rolled to a strip blank with the thickness of 1.755 mm;
and (3) continuous annealing: continuously annealing the strip blank subjected to the secondary cold rolling at 1085 ℃, wherein the strip moving speed is 1.7 m/min;
and (3) cold rolling for three times: the deflection was 20% and a finished strip with a thickness of 1.4mm was obtained.
Table 1 shows the process parameters of the treatment processes in examples 1 to 11 of the present application.
TABLE 1 Process parameters of the treatment process in examples 1 to 11 of the present application
Comparative example
Comparative example 1
Comparative example 1 differs from example 1 in that the treatment process of comparative example 1 for the strip blank is: the procedure of primary rolling, water-cooling annealing, secondary rolling, water-cooling annealing and tertiary rolling was the same as in example 1.
Comparative example 2
Comparative example 2 differs from example 1 in that the treatment process of comparative example 2 for the strip blank is: the procedure of primary rolling, continuous annealing, secondary rolling, water-cooling annealing and tertiary rolling was the same as in example 1.
Comparative example 3
Comparative example 3 differs from example 1 in that the treatment process of comparative example 3 for the strip blank is: the procedure of primary rolling, water-cooling annealing and secondary rolling was the same as in example 1.
Comparative example 4
Comparative example 4 differs from example 1 in that the treatment process of comparative example 4 for the strip blank is: the procedure of primary rolling + continuous annealing + secondary rolling was the same as in example 1.
Performance test
And (3) carrying out performance detection on the finished product strip obtained in the application to obtain the influence of the continuous annealing process in the examples 1-11 and the comparative examples 1-4 on the performance of the nickel-based high-temperature alloy strip.
(I) mechanical Property measurement
The finished tapes in examples 1 to 11 and comparative examples 1 to 4 of the application are subjected to room temperature tensile test, the detection standard is GB/T228.1-2010, and the performance detection results are shown in the following table.
TABLE 2 tensile Property parameters of the finished tapes of examples 1-11 and comparative examples 1-4
As can be seen from table 2, the tensile strength of the finished strip in example 1 is 1422MPa, the yield strength is 1257MPa, and the elongation is 23.5%, and it can be seen that the finished strip processed by continuous annealing and cold rolling has high tensile strength, high yield strength, and high elongation, so that the finished strip has good strength and plasticity, realizes good matching between strength and plasticity, improves the comprehensive mechanical properties of the finished strip, and can meet the requirements of the elastic member made of the finished strip on high strength and high plasticity.
The tensile strength of the finished strip in example 2 was 1530MPa, the yield strength was 1354MPa, and the elongation was 15.0%, which indicates that the finished strip had high strength and low elongation, and the finished strip had good strength but poor plasticity, and could not satisfy the requirements of the finished strip for strength and plasticity; the tensile strength of the finished strip in example 3 was 1298MPa, the yield strength was 1094MPa, and the elongation was 32.0%, indicating that the finished strip had lower strength, higher elongation, and good plasticity, but lower strength.
Comparing example 1 with examples 2-3, it can be seen that the comprehensive mechanical properties of the finished strip in example 1 are better than those of examples 2-3, which shows that the continuous annealing temperature affects the comprehensive mechanical properties of the finished strip, the continuous annealing temperature is low, the grain structure is fine, the strength of the finished strip is high, and the elongation is lower; the continuous annealing temperature is high, the grain structure is coarse, the strength of the finished strip is low, and the elongation is high; therefore, the comprehensive mechanical property of the finished strip can be further improved by optimizing the temperature of the continuous annealing, so that the finished strip has good strength and plasticity.
Comparing example 1 with examples 4-5, it can be seen that the comprehensive mechanical properties of the finished strip in example 1 are better than those of examples 4-5, which indicates that the tape transport speed in the continuous annealing process affects the comprehensive mechanical properties of the finished strip, and the tape transport speed in the continuous annealing process is preferred to further improve the comprehensive mechanical properties of the finished strip, so that the finished strip has good strength and plasticity.
Comparing example 1 with examples 6-7, it can be known that the comprehensive mechanical properties of the finished strip in example 1 are better than those in examples 6-7, and it can be inferred that the solution treatment has an influence on the comprehensive mechanical properties of the finished strip, the higher the temperature of the solution treatment, the smaller the amount of γ' strengthening phase redissolved into γ matrix, and the lower the hardness of the slab, so that the subsequent strip has a good softening effect; the lower the solution treatment temperature is, the more the gamma' strengthening phase is dissolved back into the gamma matrix, and the higher the hardness of the plate blank is, the influence on the subsequent cold rolling treatment is caused; therefore, the comprehensive mechanical property of the finished strip can be further improved by optimizing the temperature of the solution treatment, so that the finished strip has good strength and plasticity.
Comparing example 1 with comparative examples 1-4, it can be known that the comprehensive mechanical properties of the finished strip in example 1 are better than those of comparative examples 1-4, and it can be inferred that the preparation process of the strip in example 1 of the present application is better than those of the strip in comparative examples 1-4, which indicates that the comprehensive mechanical properties of the finished strip can be further improved through the continuous annealing and cold rolling treatment process, so that the finished strip has good strength and plasticity.
(II) grain size detection
The grain size test was performed on the finished strips of examples 1-11 and comparative examples 1-4 of the present application, and the statistical results are shown in the following table.
TABLE 3 statistics of grain size of the finished strip in examples 1-11 and comparative examples 1-4 of the present application
As can be seen from Table 3, when the grain size tests were performed on the finished strips of examples 1-11 and comparative examples 1-4, the grain size of the finished strip of example 1 reached 8, the grain size was excellent, the grains were fine, the structure distribution was uniform, and the finished strip had excellent structure uniformity.
(III) metallographic structure detection
The finished strip of example 1 was selected and observed for metallographic structure, as shown in fig. 1, it can be seen that the grain structure of the finished strip treated by the continuous annealing process was fine and uniformly distributed.
(IV) Gamma' enhanced phase scanning tissue detection
The finished product strip material in the embodiment 1 is selected, and the gamma ' strengthening phase is scanned and observed, as shown in fig. 2, it can be seen that the gamma ' strengthening phase precipitated from the finished product strip material processed by the continuous annealing process is large in quantity and uniform in distribution, so that it can be inferred that the gamma ' strengthening phase is stably precipitated by the continuous annealing, the strengthening effect of the finished product strip material is further improved, and the finished product strip material has good strength and plasticity.
The present embodiment is only for explaining the present application, and it is not limited to the present application, and those skilled in the art can make modifications of the present embodiment without inventive contribution as needed after reading the present specification, but all of them are protected by patent law within the scope of the claims of the present application.
Claims (8)
1. A preparation process of a high-strength high-elasticity high-plasticity nickel-based superalloy strip is characterized by comprising the following steps:
preparing a strip blank: smelting an alloy cast ingot, homogenizing the cast ingot, forging and cogging the homogenized cast ingot to obtain a plate blank, carrying out multi-fire hot rolling on the plate blank, and carrying out solid solution treatment on the hot-rolled plate blank;
primary cold rolling: mechanically polishing the plate blank subjected to the solution treatment and performing edge linear cutting to obtain a strip blank required by primary cold rolling, and performing primary cold rolling on the strip blank;
water cooling and annealing: carrying out water-cooling annealing on the strip blank subjected to the primary cold rolling;
secondary cold rolling: carrying out secondary cold rolling on the strip blank subjected to water-cooling annealing;
and (3) continuous annealing: carrying out continuous annealing treatment on the strip blank subjected to the secondary cold rolling;
the process parameters of continuous annealing are as follows: the continuous annealing temperature is 1050-1160 ℃, when the thickness of the finished product strip blank before cold rolling is 1.8-2.5 mm, the strip moving speed is 0.8-1.3 m/min; when the thickness of the belt blank is 1.6-1.8 mm, the belt conveying speed is 1.3-2.0 m/min; when the thickness of the belt blank is 1.3-1.6 mm, the belt conveying speed is 2.0-2.5 m/min;
and (3) cold rolling for three times: and carrying out three times of cold rolling on the strip blank after the continuous annealing to obtain a finished product strip.
2. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: in the water-cooling annealing treatment, the annealing temperature is 1070-1170 ℃, the heat preservation time is calculated according to a formula of t = (2-4) d/min (d is the blank thickness), and air cooling or water cooling is adopted after annealing.
3. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: the cold rolling deformation of the strip blank is 30-45%.
4. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: and the final cold deformation of the finished strip is 7-25%.
5. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: the temperature of the solid solution treatment is 1050-1150 ℃, the heat preservation time is 20-60 min, and the cooling mode after the solid solution treatment adopts water cooling.
6. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: the homogenization treatment temperature of the alloy ingot is 1160-1190 ℃, and the heat preservation time is calculated according to a formula of t = (13-20) d min/mm (d is the diameter of the alloy ingot).
7. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: the hot rolling heating temperature is 1100-1200 ℃, the primary heating heat preservation time is 2-3h, and the subsequent hot rolling heating heat preservation time is calculated according to the thickness of the blank and a formula of t = (1.5-3.0) d/min (d is the thickness of the blank).
8. The preparation process of the high-strength high-elasticity high-plasticity nickel-based superalloy strip according to claim 1, wherein the preparation process comprises the following steps: the hot rolling deformation is 15-25%, and each hot rolling pass is 1-2.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011638416.8A CN112813369B (en) | 2020-12-31 | 2020-12-31 | High-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and preparation process thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011638416.8A CN112813369B (en) | 2020-12-31 | 2020-12-31 | High-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and preparation process thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112813369A true CN112813369A (en) | 2021-05-18 |
| CN112813369B CN112813369B (en) | 2022-04-12 |
Family
ID=75857761
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011638416.8A Active CN112813369B (en) | 2020-12-31 | 2020-12-31 | High-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and preparation process thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112813369B (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114196803A (en) * | 2021-11-16 | 2022-03-18 | 北京钢研高纳科技股份有限公司 | GH2132 alloy asymmetric-section profiled wire for fastener and preparation method thereof |
| CN114540730A (en) * | 2021-12-31 | 2022-05-27 | 北京钢研高纳科技股份有限公司 | High-quality nickel-chromium-iron-based high-temperature alloy plate and preparation method thereof |
| CN115786773A (en) * | 2022-11-25 | 2023-03-14 | 北京钢研高纳科技股份有限公司 | Nickel-based corrosion-resistant alloy thin strip and preparation method thereof |
| CN117683989A (en) * | 2024-02-02 | 2024-03-12 | 成都先进金属材料产业技术研究院股份有限公司 | High-temperature alloy sheet and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5867854A (en) * | 1981-10-16 | 1983-04-22 | Sumitomo Metal Ind Ltd | Preparation of nickel base high chromium alloy excellent in stress, corrosion cracking resistance |
| CN106676331A (en) * | 2016-12-22 | 2017-05-17 | 钢铁研究总院 | High-temperature-resistant high-elastic nickel-chromium alloy strip and preparation method thereof |
| CN109468561A (en) * | 2018-11-27 | 2019-03-15 | 中国航发沈阳黎明航空发动机有限责任公司 | A kind of preparation method of GH3625 alloy strip steel rolled stock |
| CN111112333A (en) * | 2019-12-28 | 2020-05-08 | 北京北冶功能材料有限公司 | Preparation method of nickel-chromium-based precision resistance alloy foil |
-
2020
- 2020-12-31 CN CN202011638416.8A patent/CN112813369B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5867854A (en) * | 1981-10-16 | 1983-04-22 | Sumitomo Metal Ind Ltd | Preparation of nickel base high chromium alloy excellent in stress, corrosion cracking resistance |
| CN106676331A (en) * | 2016-12-22 | 2017-05-17 | 钢铁研究总院 | High-temperature-resistant high-elastic nickel-chromium alloy strip and preparation method thereof |
| CN109468561A (en) * | 2018-11-27 | 2019-03-15 | 中国航发沈阳黎明航空发动机有限责任公司 | A kind of preparation method of GH3625 alloy strip steel rolled stock |
| CN111112333A (en) * | 2019-12-28 | 2020-05-08 | 北京北冶功能材料有限公司 | Preparation method of nickel-chromium-based precision resistance alloy foil |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114196803A (en) * | 2021-11-16 | 2022-03-18 | 北京钢研高纳科技股份有限公司 | GH2132 alloy asymmetric-section profiled wire for fastener and preparation method thereof |
| CN114196803B (en) * | 2021-11-16 | 2024-04-19 | 北京钢研高纳科技股份有限公司 | GH2132 alloy asymmetric-section special-shaped wire for fastener and preparation method thereof |
| CN114540730A (en) * | 2021-12-31 | 2022-05-27 | 北京钢研高纳科技股份有限公司 | High-quality nickel-chromium-iron-based high-temperature alloy plate and preparation method thereof |
| CN115786773A (en) * | 2022-11-25 | 2023-03-14 | 北京钢研高纳科技股份有限公司 | Nickel-based corrosion-resistant alloy thin strip and preparation method thereof |
| CN115786773B (en) * | 2022-11-25 | 2024-03-26 | 北京钢研高纳科技股份有限公司 | Nickel-based corrosion-resistant alloy thin strip and preparation method thereof |
| CN117683989A (en) * | 2024-02-02 | 2024-03-12 | 成都先进金属材料产业技术研究院股份有限公司 | High-temperature alloy sheet and preparation method thereof |
| CN117683989B (en) * | 2024-02-02 | 2024-04-30 | 成都先进金属材料产业技术研究院股份有限公司 | High-temperature alloy sheet and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112813369B (en) | 2022-04-12 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112813369B (en) | High-strength high-elasticity high-plasticity nickel-based high-temperature alloy strip and preparation process thereof | |
| EP2075348B1 (en) | Method of manufacturing an aluminum alloy sheet for cold press forming and cold press forming method for aluminum alloy sheet | |
| CN110923525B (en) | Preparation process of high-performance 7-series aluminum alloy sheet | |
| CN101899632B (en) | Production method of 3003 aluminum alloy deep-drawing wafer | |
| CN105063430A (en) | 3003-H16 aluminum alloy plate strip and production method thereof | |
| CN108611563A (en) | A kind of CSP flows excellent formability energy mild steel steel plate and its manufacturing method | |
| CN111118422A (en) | Preparation method of high-tungsten high-cobalt nickel alloy fine-grain plate | |
| CN115896419A (en) | Preparation method and application of GH2132 alloy bar | |
| CN113308653B (en) | Aluminum lithium alloy heat treatment preparation method based on spray forming | |
| JPH06240424A (en) | Production of aluminum alloy sheet excellent in formability and baking hardenability | |
| CN102676913B (en) | Cold-rolled steel strip for flux-cored wire and production method of cold-rolled steel strip | |
| CN116727443A (en) | Nickel-based alloy coiled plate and production method thereof | |
| CN114231869B (en) | Near-alpha type high-temperature titanium alloy strip and preparation method thereof | |
| CN113073186B (en) | Method for improving cold rolling quality of Cu-containing high-strength non-oriented silicon steel | |
| CN115491474A (en) | Cold rolling preparation method of GH696 high-temperature alloy strip for spring | |
| CN114672751A (en) | Heat treatment process of high-strength and high-hardness Cu-Ni-Co-Si alloy strip | |
| CN109487131B (en) | Production method of aluminum alloy base material for 5052 alloy door plate | |
| CN112853230B (en) | Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof | |
| JPH07228957A (en) | Production of aluminum alloy sheet having excellent formability and quench-hardenability | |
| TW201918567A (en) | Dual phase steel and method of forming the same | |
| JP2003231956A (en) | PROCESS FOR MANUFACTURING Al-Mg-Cu ALUMINUM ALLOY PLATE FOR FABRICATION | |
| CN115369293B (en) | High-strength Al-Mg aluminum plate strip for anodic oxidation and preparation method thereof | |
| CN111270113B (en) | Production process of 5052 aluminum alloy plate with low earing rate | |
| CN112742871B (en) | High-efficiency 6000-series aluminum alloy medium plate hot rolling method | |
| CN116574984A (en) | Manufacturing method of 6082 alloy T6 state coil heat treatment aging |
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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |