CN115852283A - High-strength plastic nickel-based alloy plate with double-peak structure and preparation method thereof - Google Patents
High-strength plastic nickel-based alloy plate with double-peak structure and preparation method thereof Download PDFInfo
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Abstract
The invention belongs to the technical field of metal material heat treatment, and particularly relates to a high-strength plastic nickel-based alloy plate with a bimodal structure and a preparation method thereof.
Description
Technical Field
The invention relates to the technical field of metal material heat treatment, in particular to a high-strength plastic nickel-based alloy plate with a double-peak structure and a preparation method thereof.
Background
For typical solution strengthened nickel-based alloys, elongation can reach higher levels, but due to limited solution strengthening of the solution atoms, yield strength is moderate, and while fine grain strengthening can improve its strength and toughness properties, work hardening capacity and elongation are reduced. This requires that we find a suitable process to adjust the microstructure of the material so that the material has a better strength-to-plasticity ratio. The bimodal structure is used for improving the strong plasticity of the material by introducing two grains with different sizes, and is an important performance regulation means.
The prior art discloses the study and discovery of bimodal structures on different metals. For example by cold rolling and annealing in CoCrFeNiMo 0.2 Typical incomplete recrystallization texture is realized in the high-entropy alloy, the size of small grains can reach about several micrometers, and the size of large grains can reach about 100 micrometers. On the premise of keeping the strength of the material, the elongation is improved by 30 percent. The main reasons for improving the strength of the sample are large-grain internal dislocation strengthening and fine-grain strengthening, and the volume fraction of the recrystallized fine grains with high proportion is beneficial to improving the work hardening capacity of the alloy, so the elongation is higher. As another example, annealing cold rolled CP-Ti alloys at different temperatures, partially recrystallized to form a bimodal structure (equiaxed and elongated grains) exhibiting an excellent combination of ultimate tensile strength (UTS: 702 MPa) and total elongation (EL: 36.4%); both of the above-mentioned preparation methods obtain a bimodal structure by cold rolling and annealing, which contributes to obtaining an excellent combination of high strength and good plasticity. The above-mentioned preparation method cannot achieve the desired effect when applied to the nickel-based alloy sheet. Chinese patent document CN107034408A discloses a preparation method of grain size bimodal distribution in high entropy alloy, but the method used is ball milling, sintering and annealing process, and belongs to the field of powder metallurgy. Therefore, from the application field, the method cannot be applied to the fields of rolling and heat treatment of metal plates; chinese patent document CN110396633B discloses a preparation method of an entropy alloy in an ultra-fine grain bimodal structure, wherein the final product obtains the distribution characteristics of micron and nanometer bimodal grain sizes through hot rolling, deep cold rolling and annealing, the above patent belongs to the technical field of metal plate strip rolling and heat treatment, although the invention can be applied to the bimodal structure preparation of single-phase face-centered cubic alloy, the invention is used for nickel-based bimodal structure preparation of nickel-based face-centered cubic alloyThe alloy sheet cannot achieve a desired effect.
Disclosure of Invention
In order to solve the problems in the prior art, the invention mainly aims to provide a high-strength plastic-nickel-based alloy plate with a bimodal structure and a preparation method thereof.
To solve the above technical problem, according to an aspect of the present invention, the present invention provides the following technical solutions:
a preparation method of a high-strength plastic-nickel base alloy plate with a bimodal structure comprises the following steps:
s1, solution treatment
Heating the nickel-based alloy to 1120-1150 ℃, preserving heat for 8-13min, and then quenching to room temperature;
s2, cold rolling
Cold rolling the nickel-based alloy subjected to solution treatment, wherein the cold rolling temperature is room temperature, and the total reduction is 55-65%;
s3, annealing
And (3) placing the cold-rolled sheet into a heating furnace, heating to 800-850 ℃, keeping the temperature for 9-12min, and then cooling to room temperature in air.
The preferable scheme of the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure is as follows: the nickel-based alloy is N06625 nickel-based alloy.
The preferable scheme of the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure is as follows: in the step S1, the heating rate is 7 to 10 ℃/min.
The preferable scheme of the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure is as follows: in the step S1, the average grain size of the nickel-based alloy after the solution treatment is 100 to 105 μm.
The preferable scheme of the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure is as follows: in the step S2, the reduction per pass is 8% -10%.
As a preferred scheme of the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure, the preparation method comprises the following steps: in the step S3, the heating rate is 8 to 11 ℃/min.
The preferable scheme of the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure is as follows: the high-strength plastic nickel-based alloy plate comprises two bimodal structures: one is a combination of 2 to 6 mu m of crystal grains and 90 to 95 mu m of crystal grains, and the other is a combination of 2 to 5 mu m of crystal grains and 6 to 18 mu m of crystal grains.
In order to solve the above technical problem, according to another aspect of the present invention, the present invention provides the following technical solutions:
a high-strength plastic-nickel-based alloy plate with a double-peak structure is prepared by the preparation method.
As a preferred scheme of the high-strength plastic nickel-based alloy plate with the bimodal structure, the high-strength plastic nickel-based alloy plate comprises the following components in percentage by weight: the high-strength plastic nickel-based alloy plate comprises two bimodal structures: one is a combination of 2 to 6 mu m crystal grains and 90 to 95 mu m crystal grains, and the other is a combination of 2 to 5 mu m crystal grains and 6 to 18 mu m crystal grains.
The preferable scheme of the high-strength plastic nickel-based alloy plate with the bimodal structure is as follows: the tensile strength of the high-strength plastic-nickel base alloy plate is more than or equal to 990MPa, the yield strength is more than or equal to 560MPa, and the elongation is more than or equal to 65%.
The invention has the following beneficial effects:
the invention provides a high-strength plastic nickel-based alloy plate with a bimodal structure and a preparation method thereof, the high-strength plastic nickel-based alloy plate with the bimodal structure is prepared by adopting the processes of solution treatment, cold rolling and annealing, the strength and the plasticity of the nickel-based alloy plate are simultaneously improved, the tensile strength is more than or equal to 990MPa, the yield strength is more than or equal to 560MPa, and the elongation is more than or equal to 65%.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, it is obvious that the drawings in the following description are only some embodiments of the present invention, and for those skilled in the art, other drawings can be obtained according to the structures shown in the drawings without creative efforts.
FIG. 1 is a microstructure and topography of a nickel-base alloy sheet prepared according to an embodiment of the present invention;
FIG. 2 is an optical microstructure of a nickel-base alloy sheet prepared in example 1 of the present invention;
FIG. 3 is an EBSD microstructure of a nickel-based alloy plate prepared in example 1 of the present invention;
FIG. 4 is a bimodal microstructure distribution plot of a nickel-base alloy sheet prepared in example 1 of the present invention;
FIG. 5 is an optical microstructure of a nickel-base alloy sheet prepared in example 2 of the present invention;
FIG. 6 is an EBSD microstructure of a nickel-based alloy plate prepared in example 2 of the present invention;
FIG. 7 is a bimodal microstructure distribution plot of a nickel-base alloy sheet prepared in example 2 of the present invention;
FIG. 8 is a tensile curve of nickel-base alloy sheet materials prepared in examples 1 and 2 of the present invention;
FIG. 9 is a comparison graph of mechanical properties of the nickel-based alloy N06625 under different processes.
The implementation, functional features and advantages of the present invention will be further described with reference to the accompanying drawings.
Detailed Description
The following will clearly and completely describe the technical solutions in the embodiments, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments. All other embodiments, which can be obtained by a person skilled in the art without inventive step based on the embodiments of the present invention, are within the scope of protection of the present invention.
The invention provides a high-strength plastic nickel-based alloy plate with a bimodal structure and a preparation method thereof.
According to one aspect of the invention, the invention provides the following technical scheme:
a preparation method of a high-strength plastic-nickel base alloy plate with a bimodal structure comprises the following steps:
s1, solution treatment
Heating the nickel-based alloy to 1120-1150 ℃, preserving heat for 8-13min, and then quenching to room temperature;
s2, cold rolling
Cold rolling the nickel-based alloy subjected to solution treatment, wherein the cold rolling temperature is room temperature, and the total reduction is 55-65%;
s3, annealing
And (3) placing the cold-rolled sheet into a heating furnace, heating to 800-850 ℃, keeping the temperature for 9-12min, and then cooling to room temperature in air.
Furthermore, the nickel-based alloy is N06625, has a single-phase face-centered cubic structure, and has uneven grain size.
Further, in the step S1, the heating rate is 7 to 10 ℃/min; the average grain size of the nickel-based alloy after the solution treatment is 95 to 105 mu m. Specifically, the heating rate may be, for example, but not limited to, any one of 7 ℃/min, 8 ℃/min, 9 ℃/min, 10 ℃/min, or a range between any two; the heating temperature may be, for example, but is not limited to, any one of 1120 ℃, 1125 ℃, 1130 ℃, 1135 ℃, 1140 ℃, 1145 ℃ and 1150 ℃ or a range between any two of them; the holding time may be, for example, but not limited to, any one of 8min, 9min, 10min, 11min, 12min, 13min or a range between any two; the average grain size of the nickel-base alloy after solution treatment may be, for example, but not limited to, any one or a range between any two of 95 μm, 96 μm, 97 μm, 98 μm, 99 μm, 100 μm, 101 μm, 102 μm, 103 μm, 104 μm, 105 μm; since the nickel-base alloy after forging is not completely recrystallized sufficiently, the grain size distribution is disordered, and many carbides are present, so that direct cold rolling cannot be performed. The solution treatment can avoid the adverse effect on the mechanical properties of the material after cold rolling and annealing due to the disorder of the grain size and the existence of carbides. Meanwhile, the crystal grain size after the solution treatment is uniform and is 100-105 mu m in average, the large crystal grain size and the large reduction rate can improve the occurrence of crystal grain crushing and cold rolling nonuniform strain, and the effects on the generation of small-size crystal grains and the maintenance of large crystal grains during annealing are certain.
Further, in step S2, before cold rolling, the material after solution treatment is first subjected to acid washing to remove the scale, so as to ensure that the surface of the steel plate is smooth, prevent the plate from being uneven in thickness due to foreign matters during cold rolling, avoid damaging the rollers, and prevent the scale from generating adverse effects in subsequent rolling. The reduction of each pass of the cold rolling is 8-10%, the rolling speed is 0.4-0.7 m/s, the reduction of each pass and the total reduction are mainly in consideration of the strain accumulation effect in the cold rolling process, the requirement of strain accumulation is not facilitated due to too low reduction, and the rolling difficulty is increased due to too high reduction, so that rollers can be damaged. Specifically, the reduction per pass may be, for example, but not limited to, any one of 8%, 8.5%, 9%, 9.5%, 10%, or a range between any two; the rolling speed may be, for example, but not limited to, any one of 0.4m/s, 0.5m/s, 0.6m/s, 0.7m/s, or a range between any two; the total reduction may be, for example, but not limited to, any one of 55%, 56%, 57%, 58%, 59%, 60%, 61%, 62%, 63%, 64%, 65%, or a range between any two;
further, in the step S3, the heating rate is 8 to 11 ℃/min. Specifically, the heating rate may be, for example, but not limited to, any one of 8 ℃/min, 9 ℃/min, 10 ℃/min, 11 ℃/min, or a range between any two; the heating temperature may be, for example, but is not limited to, any one of 800 ℃, 810 ℃, 820 ℃, 830 ℃, 840 ℃, 850 ℃ or a range between any two; the incubation time may be, for example, but is not limited to, any one of 9min, 10min, 11min, 12min or a range between any two; the annealing at a lower temperature is selected, so that the process of partial recrystallization of the cold-rolled structure is realized, and the formation of a bimodal structure is facilitated. Meanwhile, the heat preservation time cannot be too short or too long, the proportion of partial recrystallization is too low due to the too short time, and the proportion of the bimodal structure cannot reach the optimal proportion. If the time is too long, the tissues grow up, which is not favorable for the formation of bimodal tissues.
Preferably, the bimodal structure of the high-strength plastic nickel-base alloy sheet material comprises two types: one is a combination of 2 to 6 mu m of crystal grains and 90 to 95 mu m of crystal grains, and the other is a combination of 2 to 5 mu m of crystal grains and 6 to 18 mu m of crystal grains.
Preferably, the tensile strength of the high-strength plastic-nickel base alloy plate is greater than or equal to 990MPa, the yield strength is greater than or equal to 560MPa, and the elongation is greater than or equal to 65%.
By adopting the preparation method, two different bimodal structures are obtained in the nickel-based alloy plate structure. For different crystal grain Taylor factors in the cold rolling process of the solid solution strengthening type nickel base alloy, according to Taylor principle, the crystal grain with higher Taylor coefficient is difficult to deform when the metal is subjected to plastic deformation, and similarly, the lower the Taylor coefficient, the more easily the crystal grain accommodates more strain in the crystal grain through dislocation slip or rotation. This allows the metal to store more external strained grains to form the SD (vice-versa) region when more strain occurs, and conversely to form the WD (Weak deformation) region. This phenomenon is more likely to occur during large deformation of the metal. The low-temperature static recrystallization converts the cold-rolled microstructure in which the SD region and the WD region coexist into a different type of structure. Generally, during the low temperature annealing and early annealing, recrystallized grains essentially nucleate in the high strain region because the high energy stored in the SD region provides the motive force for nucleation of recrystallization. This results in a large number of recrystallization nucleation occurring simultaneously in this region, forming a cluster of fine recrystallized grain clusters in the high strain region SD. This results in the nickel-base alloy sheet after annealing at 800 c forming the texture shown in fig. 1, with fine grains and large deformed grains existing in the matrix. For the WD region, it is believed that the double boundaries and deformation zone, which are nucleation sites, are limited, which results in that when the temperature is further increased, the WD region also starts to recrystallize, and that the number of recrystallized grains formed in the WD region is small, the grain size is large, and the grains appear as substantially equiaxed recrystallized grains, but with a distinct difference in size. In summary, the solution treatment is performed to obtain large grains, the cold rolling is performed to obtain a non-uniform microstructure, and the low-temperature annealing is performed to the cold-rolled material to obtain a microstructure with bimodal grains.
The technical solution of the present invention is further illustrated by the following specific examples.
Example 1
A preparation method of a high-strength plastic-nickel base alloy plate with a bimodal structure comprises the following steps:
s1, solution treatment
Heating the nickel-based alloy to 1130 ℃ at a heating rate of 10 ℃/min, preserving heat for 10min, and then quenching to room temperature; the nickel-based alloy is N06625, wherein the atomic percentages of main components of Ni, cr and Mo are 62%, 23% and 8%. The length, the width and the height of the nickel-based alloy sample are respectively 130mm, 40mm and 5mm; the grain size of the nickel base alloy after the solution treatment is kept about 100 μm.
S2, cold rolling
Cold rolling the nickel-based alloy subjected to solution treatment, wherein the cold rolling temperature is room temperature, the single-pass reduction of the cold rolling is 10%, the nickel-based alloy is rolled to 2mm, and the total reduction is 60%;
s3, annealing
And (3) placing the cold-rolled plate into a heating furnace, heating to 800 ℃ at the heating rate of 10 ℃/min, preserving the heat for 10min, and then air-cooling to room temperature. The optical microstructure of the nickel-based alloy plate prepared in the embodiment is shown in figure 2, the EBSD microstructure is shown in figure 3, and bimodal grain size distribution with the average grain diameter of 2-6 μm and the average grain diameter of 90-95 μm is obtained in the structure, as shown in figure 4.
Example 2
A preparation method of a high-strength plastic-nickel base alloy plate with a bimodal structure comprises the following steps:
s1, solution treatment
Heating the nickel-based alloy to 1130 ℃ at a heating rate of 10 ℃/min, preserving heat for 10min, and then quenching to room temperature; the nickel-based alloy is N06625, wherein the atomic percentages of main components of Ni, cr and Mo are 62%, 23% and 8%. The length, the width and the height of the nickel-based alloy sample are respectively 130mm, 40mm and 5mm; the grain size of the nickel base alloy after the solution treatment is kept about 100 μm.
S2, cold rolling
Cold rolling the nickel-based alloy subjected to solution treatment, wherein the cold rolling temperature is room temperature, the single-pass reduction of the cold rolling is 10%, the nickel-based alloy is rolled to 2mm, and the total reduction is 60%;
s3, annealing
And (3) putting the cold-rolled plate into a heating furnace, heating to 850 ℃ at a heating rate of 10 ℃/min, preserving heat for 10min, and then air-cooling to room temperature. The optical microstructure of the nickel-based alloy plate prepared in the embodiment is shown in fig. 5, the EBSD microstructure is shown in fig. 6, and the bimodal grain size distribution with average grains of 2-5 μm and average grain diameters of 6-18 μm is obtained in the microstructure, as shown in fig. 7.
The nickel-base alloy sheets prepared in examples 1 and 2 were subjected to a tensile test, and the tensile curve thereof is shown in fig. 8; a comparison graph of the mechanical properties of nickel base alloy N06625 under different processes (including examples 1 and 2) is shown in fig. 9. As can be seen from fig. 9, the mechanical properties of the nickel-based alloy sheet prepared in the embodiment of the present invention are significantly better than those of the nickel-based alloy sheet prepared in the other processes, and as can be seen from fig. 8, the tensile properties of the nickel-based alloy sheet prepared in the present invention are as follows, wherein the tensile strength of example 1 is 1010MPa, the yield strength is 613MPa, the elongation is 68.6%, the tensile strength of example 2 is 995MPa, the yield strength is 567MPa, and the elongation is 71.5%. The strength and the plasticity of the nickel-based alloy plate are simultaneously improved, and the nickel-based alloy plate is convenient for large-scale industrial production and application.
The above description is only a preferred embodiment of the present invention, and is not intended to limit the scope of the present invention, and all equivalent structural changes made by using the content of the present specification or other related technical fields within the spirit of the present invention are included in the scope of the present invention.
Claims (10)
1. The preparation method of the high-strength plastic-nickel-based alloy plate with the bimodal structure is characterized by comprising the following steps of:
s1, solution treatment
Heating the nickel-based alloy to 1120-1150 ℃, preserving heat for 8-13min, and then quenching to room temperature;
s2, cold rolling
Cold rolling the nickel-based alloy subjected to solution treatment, wherein the cold rolling temperature is room temperature, and the total reduction is 55-65%;
s3, annealing
And (3) placing the cold-rolled sheet into a heating furnace, heating to 800-850 ℃, keeping the temperature for 9-12min, and then cooling to room temperature in air.
2. The method of making a high strength plastic nickel-base alloy sheet having a bimodal texture as claimed in claim 1, wherein the nickel-base alloy is N06625.
3. The method for preparing the high-strength plastic-nickel-base alloy plate with the bimodal structure as claimed in claim 1, wherein in the step S1, the heating rate is 7-10 ℃/min.
4. The method for preparing a high-strength plastic nickel-based alloy plate with a bimodal structure as claimed in claim 1, wherein in the step S1, the average grain size of the nickel-based alloy after solution treatment is 100-105 μm.
5. The method for preparing the high-strength plastic-nickel-base alloy plate with the bimodal structure as claimed in claim 1, wherein in the step S2, the reduction per pass is 8% -10%.
6. The method for preparing the high-strength plastic-nickel-based alloy plate with the bimodal structure as claimed in claim 1, wherein in the step S3, the heating rate is 8-11 ℃/min.
7. The method for preparing a high-strength nickel-base alloy sheet having a bimodal structure as claimed in claim 1, wherein the bimodal structure of the high-strength nickel-base alloy sheet includes two types: one is a combination of 2 to 6 mu m of crystal grains and 90 to 95 mu m of crystal grains, and the other is a combination of 2 to 5 mu m of crystal grains and 6 to 18 mu m of crystal grains.
8. A high-strength plastic nickel-based alloy plate with a bimodal structure is characterized by being prepared by the preparation method of the high-strength plastic nickel-based alloy plate with the bimodal structure as claimed in any one of claims 1 to 7.
9. The high strength nickel-base alloy sheet with a bimodal structure as claimed in claim 8, wherein the bimodal structure of the high strength nickel-base alloy sheet comprises two: one is a combination of 2 to 6 mu m of crystal grains and 90 to 95 mu m of crystal grains, and the other is a combination of 2 to 5 mu m of crystal grains and 6 to 18 mu m of crystal grains.
10. The high-strength plastic-nickel-base alloy plate with the bimodal structure as claimed in claim 8, wherein the tensile strength of the high-strength plastic-nickel-base alloy plate is more than or equal to 990MPa, the yield strength of the high-strength plastic-nickel-base alloy plate is more than or equal to 560MPa, and the elongation of the high-strength plastic-nickel-base alloy plate is more than or equal to 65%.
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