Activators, repair agents and repair methods for reshaping damaged defects in leaves

Abstract

The application discloses an activator, a repairing agent and a repairing method for blade damage defect shape and property remodeling, relates to the nickel-based high-temperature alloy remodeling technical field, and the preparation of the activator at least includes the following mass percentages of elements: Cr (16.1%-19.8%), Co (9.2%-12.8%), Al (1.2%-2.7%), Ti (9.6%-11.7%), Nb (5.6%-7.3%), Ru (4.6%-5.8%), Mg (0.005%-0.01%); the repairing agent includes the activator, a curing agent and an adhesive which are uniformly mixed in proportion; the application can effectively improve the creep resistance and mechanical properties of the alloy at high temperature, and can effectively avoid the generation of more pores in the shape and property remodeling area caused by the early solidification and closure of the capillary channel.

Description

TECHNICAL FIELD

[0001] The present application relates to the technical field of nickel-based superalloy repair, in particular to an activator for reshaping of blade damage defects, a repair agent and a repair method. BACKGROUND

[0002] The nickel-based superalloy Inconel738LC (IN738LC) is an equiaxed crystal alloy with nominal chemical composition of Ni-16wt%Cr-8.5wt%Co-2.5wt%W-3.5wt%Al-3.5wt%Ti-1.7wt%Ta-1.7wt%Mo-0.8wt%Nb-0.09wt%C-0.01wt%B-0.05wt%Zr, which has good microstructure stability and casting process performance, and can be used for producing aero-engine and gas turbine precision cast blades. During the service process of turbine blades, it is inevitable that the surface shape of the blades is damaged due to long-term corrosion and erosion of high-temperature gas and cold and hot fatigue. Adopting an effective repair method to repair the damaged parts can effectively prolong the service life of the blades and reduce the operation and maintenance cost.

[0003] For Inconel738LC nickel-based superalloy blades with high Al and Ti content, the conventional melting welding repair is prone to cause cracking of the base material. In the field of nickel-based superalloy repair, powder metallurgy technology is particularly suitable for repair and remanufacturing of high-aluminum and titanium content cast high-temperature alloys. This technology is based on the principle of isothermal solidification, which can effectively avoid the generation of thermal cracks in the repair area, and has many advantages such as low cost and high efficiency. The repair material used is a mixture of a low-melting-point activator for brazing and a high-melting-point solidifying agent for filling, and a binder is added to make a paste which is coated on the surface of the workpiece and subjected to metallurgical sintering in a vacuum furnace, so as to realize the reshaping of the damaged area.

[0004] Patents CN114669820A, CN114632991A and CN114669956A respectively report several powder metallurgy repair materials for IN738 alloy, and the highest room temperature tensile strength of the repaired joint is 723 MPa. In order to ensure that the above solder can be completely liquefied at a temperature lower than the initial melting point of the base material, the melting point suppression effect of the solder is achieved by introducing high concentrations of B (CN114669820A), Zr (CN114669956A) and Hf (CN114632991A). Although the process of the solder is guaranteed, there is a large difference in element composition and microstructure between the solder and the base material, and a large number of boride brittle phases and B-rich, Zr-rich and Hf-rich low-melting eutectic phases are generated in the shape and property remodeling area, which will cause: 1) these low-melting harmful phases will melt at the solution heat treatment temperature (about 1130℃) of IN738LC nickel-based high-temperature alloy blade, in order to prevent the solution heat treatment from causing the shape and property remodeling area to be remelted, the solution heat treatment temperature needs to be reduced, which will cause the blade matrix to be unable to achieve the best recovery heat treatment effect, resulting in a decrease in the mechanical properties of the matrix; 2) boride and B-rich, Zr-rich and Hf-rich eutectic phases are brittle phases and are difficult to eliminate through heat treatment, and large-scale precipitation and connection into sheets will cause a serious decrease in the high-temperature mechanical properties of the shape and property remodeling area, so it cannot be used for repairing blades in high-stress working conditions, which limits its application range to some extent; 3) the B in the shape and property remodeling area of the blade repaired using the B-rich repair material will diffuse to the coating during service, causing the coating of the blade to fail prematurely. SUMMARY

[0005] The purpose of the present application is to provide an activator, a repair agent and a repair method for shape and property remodeling of blade damage defects, which can effectively improve the creep resistance and mechanical properties of the alloy at high temperatures, and can effectively avoid the premature solidification and closure of capillary channels to cause the shape and property remodeling area to generate more pores.

[0006] The technical scheme adopted by the present application is as follows: an activator for shape and property remodeling of blade damage defects, applied to a nickel-based nickel-based high-temperature alloy blade, the preparation of the activator comprises at least the following elements with the following mass percentages:

[0007] Cr (16.1%-19.8%), Co (9.2%-12.8%), Al (1.2%-2.7%), Ti (9.6%-11.7%), Nb (5.6%-7.3%), Ru (4.6%-5.8%), Mg (0.005%-0.01%); the remainder is Ni or / and unavoidable impurity elements.

[0008] Further, the activator is prepared by a rotating electrode method.

[0009] Further, the melting temperature range of the activator is 1131℃-1160℃.

[0010] Further, the particle size of the activator is 23μm-30μm.

[0011] A repairing agent for reshaping of blade damage defect, comprising a curing agent, a binder and the activator, the activator, the curing agent and the binder being mixed uniformly in proportion.

[0012] Further, the activator, the curing agent and the binder are mixed uniformly in proportion of 3:6:1 in mass ratio; the curing agent is a de-titanium GTD111 commercial custom alloy powder; and the binder is a NICROBRAZ S-BINDR type commercial binder.

[0013] A repairing method for reshaping of blade damage defect, comprising the following steps:

[0014] S1: preparing the repairing agent;

[0015] S2: shaping of blade defect;

[0016] applying the repairing agent obtained in step S1 to the damage defect of the nickel-based high-temperature alloy blade;

[0017] S3: reshaping of blade shape;

[0018] performing heat preservation on the blade after step S2 in a vacuum environment, and after the heat preservation is completed, furnace cooling is performed, and after cooling, heat treatment and shaping are performed on the blade, so that the reshaping of the damage defect is completed.

[0019] Further, in step S2, before the repairing agent is applied, the damage defect needs to be cleaned in step S21.

[0020] S21: cleaning; polishing the oxide layer at the damage defect, and then placing the damage defect in an alcohol or acetone solution for ultrasonic cleaning, and after cleaning, low-temperature drying is performed.

[0021] Further, in step S3, the vacuum degree of the vacuum environment is better than 1x10 -3 Pa;

[0022] Further, in step S3, the heat preservation temperature is 1190℃-1220℃, and the heat preservation time is 45min-75min.

[0023] According to the above technical scheme, the present application has the following beneficial effects:

[0024] 1. The activator provided by the application does not add B, Zr, Hf and other melting point inhibitors, but realizes the melting point inhibition of the activator material by proportion control of the necessary alloying elements of the nickel-based superalloy, which effectively avoids the generation of boride brittle phase and low melting point eutectic phase rich in B, Zr, Hf and the like, and can significantly improve the high temperature mechanical properties of the IN738LC alloy blade shape remodeling area;

[0025] 2. The repair agent provided by the application is a clever combination of the activator and the selected curing agent, and the content of the shape remodeling area solid solution strengthening element and the gamma prime phase obtained is close to that of the base material, which will make the obtained shape remodeling area organization form consistent with the base material, and can significantly improve the high temperature mechanical properties of the shape remodeling area;

[0026] 3. The activator provided by the application introduces Ru, which is used to reduce the segregation concentration of TCP phase forming elements such as Co, Cr, Ti and Nb on the gamma / gamma prime phase interface, effectively inhibits the TCP precipitation behavior, and significantly improves the organizational stability of the metallurgical bonding area; and Ru and W elements have similar effects, the Ru element with large atomic radius is mainly solid-solved in the matrix gamma phase, which can significantly improve the high temperature creep resistance of the alloy;

[0027] 4. The activator powder provided by the application has a near-equal diameter, which can realize near-isothermal and isochronal melting in the heat preservation stage, is beneficial to the liquid phase filling of the gap between the solidified agent powder and the base material interface and the gap between the solidified agent powders, and can effectively avoid the premature solidification closure of the capillary channel to cause more pores in the shape remodeling area. BRIEF DESCRIPTION OF DRAWINGS

[0028] The application will be described by way of example and with reference to the accompanying drawings, in which:

[0029] Figure 1 DSC curve of the activator disclosed by the application;

[0030] Figure 2 Microscopic morphology of the activator disclosed by the application;

[0031] Figure 3 Macroscopic organizational morphology of the IN738LC high-temperature alloy after shape remodeling disclosed by the application;

[0032] Figure 4 Microscopic organizational morphology of the IN738LC high-temperature alloy after shape remodeling disclosed by the application. DETAILED DESCRIPTION

[0033] All features disclosed in this specification, or the steps of any method or process disclosed, may be combined in any combination, except combinations where at least some features and / or steps are mutually exclusive.

[0034] Any feature disclosed in this specification, unless otherwise stated, may be replaced by other equivalent or similar features. That is, unless otherwise stated, each feature is only an example of a series of equivalent or similar features.

[0035] Example 1

[0036] like Figures 1-2 As shown, an activator for reshaping blade damage defects is applied to nickel-based high-temperature alloy blades. The preparation of the activator includes the following elements in mass percentage:

[0037] Cr (16.1%-19.8%), Co (9.2%-12.8%), Al (1.2%-2.7%), Ti (9.6%-11.7%), Nb (5.6%-7.3%), Ru (4.6%-5.8%), Mg (0.005%-0.01%); the rest is Ni and / or unavoidable impurity elements.

[0038] In this embodiment, the activator is used to reshape the service defects of the IN738LC nickel-based high-temperature alloy blade. Patents CN114669820A, CN114632991A and CN114669956A also disclose several activators that can be used to repair the IN738LC alloy. The activator of the present invention is different from them in that it does not add high concentrations of B, Zr, and Hf as melting point inhibitors, thereby avoiding the formation of boride brittle phases and B-rich, Zr-rich, and Hf-rich low-melting point eutectic phases in the reshape zone. The structure and composition of the obtained reshape zone are close to those of the substrate, which can significantly improve the mechanical properties of the joint.

[0039] The elements used in the activator of this embodiment include Cr, Co, Al, Ti, Nb, Ru and Mg, and the beneficial effects are reflected in:

[0040] Cr is an important alloying element in IN738LC alloy, with a content of up to 16wt%. Its main function is to improve the alloy's high-temperature oxidation resistance and hot corrosion resistance. In order to ensure that the oxidation resistance and hot corrosion resistance of the performance remodeling zone obtained in the present invention are at the same level as those of the substrate, the Cr content in the activator of the present invention is limited to the range of 15.1wt% to 19.8wt%.

[0041] Co and the matrix element Ni are infinitely miscible, forming a continuous substitutional solid solution, which has a solid solution strengthening effect on the matrix and can reduce the matrix stacking fault energy. It has a limited effect on suppressing the melting point of the alloy, but can significantly reduce the solid solution temperature of the γ' phase. The present invention limits the Co content to a range of 9.2wt% to 12.8wt%.

[0042] Al is the main generating element of γ' phase, the high temperature creep resistance of the shape remodified zone is proportional to the amount of γ' phase in unit volume to some extent, but a large amount of addition will cause the melting point of the activator to rise sharply, therefore the content of Al is limited in the range of 1.2wt% to 2.7wt%, but this does not mean that the γ' phase content of the finally obtained shape remodified zone will be lower than that of IN738LC alloy substrate, it is emphasized that the activator of the present application contains high concentrations of Ti and Nb elements, which will replace part of Al in the γ' phase, thereby increasing the volume percentage of γ' phase.

[0043] In IN738LC alloy, Ti and Nb are both strengthening elements of γ' phase, which can change the composition of γ' phase, improve the reverse domain boundary energy of γ' phase, and improve the high temperature stability of γ' phase, thereby improving the strength and creep resistance of the shape remodified zone. In the present application, Ti and Nb are the main melting point suppression elements, the content of Ti is limited in the range of 9.6wt% to 11.7wt%, and the content of Nb is limited in the range of 5.6wt% to 7.3wt%, which cooperates with other alloy elements to suppress the melting point of the alloy within the process range, it is emphasized that excessive Ti and Nb in the activator of the present application can be balanced by the GTD111 type solidifier powder (not containing Ti and Ta) through element diffusion, so that the finally obtained shape remodified zone will not generate harmful phases due to the enrichment of Ti and Nb.

[0044] Ru is a rare earth element, which is added to improve the organizational stability of the shape remodified zone; another effect in the present application is to have a weak melting point suppression effect; at the same time, the Ru element with large atomic radius is solid-solved in the matrix γ phase, causing the lattice expansion of the matrix, increasing the long-range elastic stress field, thereby hindering the dislocation movement and reducing the elastic stress field, which can significantly improve the high temperature creep resistance of the alloy. The content of Ru in the present application is limited in the range of 4.6wt% to 5.8wt%.

[0045] Mg is a micro-alloying element, which is added in a small amount, can balance the segregation in the grain boundary, reduce the grain boundary energy, improve and refine the morphology of grain boundary carbides and other grain boundary precipitated phases, combine with harmful impurity element S to form high melting point compound MgS, weaken the harmful effect of S, play the role of purifying grain boundary, improve the grain boundary bonding force, increase the grain boundary strength, and effectively improve the tensile plasticity and stress rupture performance of the shape remodified zone. The content of Mg in the present application is limited in the range of 0.005wt% to 0.01wt%.

[0046] Example 2

[0047] On the basis of embodiment 1, in order to further clearly illustrate and explain the technical solutions of the present application, the following non-limiting embodiments are provided, and Table 1 is the embodiment and control example of the activator. The following element content data are mass percentage data.

[0048] Table 1 Embodiment and control example of the activator

[0049]

[0050] The advantages of embodiments 1-4 in this embodiment are as follows:

[0051] 1. The activator provided by the present application does not add high concentrations of B, Zr and Hf as melting point inhibitors, but realizes the melting point inhibition of the activator material by proportionally controlling the necessary alloying elements of the nickel-based superalloy, thereby avoiding the generation of boride brittle phases and low-melting eutectic phases rich in B, Zr and Hf in the heat preservation metallurgical process, which will significantly improve the high-temperature mechanical properties of the shape remanufacturing area of the IN738LC alloy blade.

[0052] 2. The activator component design provided by the present application is based on the high-entropy alloying theory, and therefore contains a high concentration of elements Cr, Co, Ti and Nb. Although the cleverly matched GTD111 type solidification agent for titanium removal can balance the element concentration in the entire shape remanufacturing area, the organization stability is low in the metallurgical bonding process, and the TCP phase has a high tendency to precipitate at high temperatures. Therefore, the activator introduces a certain amount of rare earth element Ru to reduce the segregation concentration of TCP phase forming elements such as Co, Cr, Ti and Nb on the γ / γ' two-phase interface, effectively inhibits the precipitation behavior of TCP, and significantly improves the organizational stability of the shape remanufacturing area. At the same time, the Ru element with a large atomic radius is solid-solved in the matrix γ phase, causing the lattice of the matrix to expand, increasing the long-range elastic stress field, thereby hindering the movement of dislocations and reducing the elastic stress field, which can significantly improve the high-temperature creep resistance of the alloy.

[0053] A feasible embodiment is that the activator can be prepared by a rotating electrode method, which is known to those skilled in the art, and the specific process is not described in detail in the present specification.

[0054] A feasible embodiment is that the melting temperature range of the activator is 1132-1160℃.

[0055] As shown in Figure 1 , it is the DSC curve of the activator disclosed in embodiment 1 of the present embodiment.

[0056] A feasible embodiment is that the melting temperature range of the activator is 1132-1160℃. Figure 2As shown, it is the micro-morphology of the activator disclosed in embodiment 1 of the present embodiment, the particle size of the activator is 23-30 μm, the size is nearly equal in diameter, which can realize nearly isothermal and isochronous melting in the holding stage, and is beneficial to the liquid phase filling of the gap between the interface of the solidification agent powder and the base material and the gap between the solidification agent powders, which can effectively avoid the generation of more pores in the shape remodeling area caused by the early solidification and closure of the capillary channel.

[0057] The activator disclosed in the present embodiment has wide applicability, and is used for shape remodeling of damage defects of an IN738LC alloy blade in combination with a GTD111 commercial custom alloy powder, so that the content of solid solution strengthening elements and γ' phase in the shape remodeling area is close to that of the base material, which makes the obtained shape remodeling area have a basic consistent structure with the base material, and can significantly improve the high-temperature mechanical properties of the shape remodeling area; multiple sites can be remodeled at one time, multiple blades can be remodeled, the remodeling efficiency is high, the cost is low, and the method has high industrial application value.

[0058] Embodiment 3

[0059] A repair agent for shape remodeling of blade damage defects, comprising a solidification agent, a binder and the activator described in embodiment 2 embodiment 1, the activator, the solidification agent and the binder are uniformly mixed in proportion.

[0060] Specifically, the activator powder, the solidification agent and the binder described in embodiment 1 are uniformly mixed in a mass ratio of 3:6:1 to prepare a plastic paste; the solidification agent is a de-titanium GTD111 commercial custom alloy powder, and the composition is: C (0.1 wt%), Cr (14.0 wt%), Co (9.5 wt%), Mo (1.6 wt%), W (3.8 wt%), Ta (2.8 wt%), Al (3.0 wt%), Zr (0.02 wt%), B (0.012 wt%), and the particle size is 75-150 μm; the binder is a commercial NICROBRA S-BINDR type binder.

[0061] It should be noted that the paste-shaped repair agent makes the repair agent viscous, reduces the flowability, makes the repair agent stable when it is filled in the remodeling position, avoids the repair agent from leaving the remodeling position before entering the heating and melting, and the viscous repair agent is more convenient to fill the remodeling area, which is specifically manifested as follows: the viscous repair agent has a certain flowability, when the repair agent is filled in the remodeling position, the repair agent can change its shape according to the size of the filling position due to its flowability, meet the filling of irregular remodeling areas, and completely fill the defects in the remodeling area under the action of its flowability.

[0062] In the embodiment, the repair agent is a combination of the activator and the selected curing agent, and the content of the solid solution strengthening elements and the γ' phase in the shape and property remolding region is close to that of the base material, which makes the microstructure of the shape and property remolding region consistent with that of the base material, and significantly improves the high-temperature mechanical properties of the shape and property remolding region.

[0063] Example 4

[0064] A repair method for blade damage defect shape and property remolding, comprising the following steps:

[0065] S1: preparing the repair agent as described in Example 3.

[0066] S2: shaping the blade defect; the damage defect of the IN738LC alloy blade is cleaned and then coated with the repair agent; the details are as follows:

[0067] S21: removing the oxide layer on the surface of the IN738LC alloy blade defect with a hard alloy steel drill bit, and the defect size is less than 40mm in length, 40mm in width and 5mm in height; after polishing, it is placed in an alcohol or acetone solution for ultrasonic cleaning for 60 minutes, and then taken out and dried for standby.

[0068] S22: coating the repair agent obtained in step S1 on the damage defect of the IN738LC alloy blade;

[0069] S3: blade shape and property remolding;

[0070] In a vacuum environment with a vacuum degree better than 1x10 -3 Pa, the blade completed in step S2 is subjected to heat preservation at a temperature of 1210℃ for 60 minutes, and the vacuum environment can be provided by a vacuum furnace; after heat preservation, the blade is cooled in the furnace, and then subjected to performance recovery heat treatment and shaping, so as to complete the shape and property remolding of the damage defect.

[0071] The shape and property remolding region and the blade base material are subjected to tensile test, and the test results are shown in Table 2.

[0072] Table 2 Tensile properties of shape and property remolding region and base material

[0073]

[0074] It can be seen that, by using the activator described in embodiment 1 of example 2, in combination with the curing agent and the adhesive, the damage defect of the IN738LC alloy blade is remolded, and the tensile strength of the remolded shape and property remolding region at room temperature is 864MPa, which can reach 87% of the strength of the blade base material.

[0075] The following known data is selected as a control example, and the details are as follows:

[0076] Control Example 1

[0077] Patent CN114669820A introduces a kind of repair agent and reshaping process for high-temperature alloy blade, in the embodiment, the powder A with the component of Ni-8wt.%Cr-3wt.%Co-2wt.%Al-2wt.%Ti-0.5wt.%W-0.5wt.%Mo-0.5wt.%Ta-0.5wt.%Nb-2.2wt.%B and the powder B with the component of Ni-25at.%Cr-20at.%Co-20at.%Al-5at.%W-5at.%Mo-5at.%Ta-2at.%Nb-5at.%Ti are mixed with the mass ratio of 0.3:1, then IN738LC alloy blade is reshaped, and the tensile property of reshaped area at room temperature after reshaping is 723MPa, which can only reach 70% of the strength of blade base material.

[0078] Comparative Example 2

[0079] Patent CN114632991A introduces a kind of repair process for repairing gas turbine blade based on powder metallurgy process, in the embodiment, the Hf-containing low-melting-point powder with the component of Ni-6wt.%Cr-3wt.%Co-1wt.%Al-1wt.%Ti-0.5wt.%W-0.5wt.%Mo-0.5wt.%Ta-0.5wt.%Nb-25wt.%Hf and the metal powder of multi-main-element alloy with the component of Ni-20at.%Cr-20at.%Co-20at.%Al-5at.%W-5at.%Mo-5at.%Ta-2at.%Nb-5at.%Ti are mixed with the mass ratio of 0.1:1, then IN738LC alloy blade is reshaped, and the tensile property of reshaped area at room temperature after reshaping is 683MPa, which can only reach 65% of the strength of blade base material.

[0080] Comparative Example 3

[0081] Patent CN114669956A introduces a kind of powder metallurgy repair method for repairing defects of high-temperature alloy blade, in the embodiment, the powder A with the component of Ni-12wt.%Cr-5wt.%Co-2wt.%Al-3wt.%Ti-2wt.%W-2wt.%Mo-10wt.%Zr and the powder B with the component of Ni-18at.%Cr-18at.%Co-6at.%Al-2at.%W-2at.%Mo-2at.%Ti are mixed with the mass ratio of 0.15:1, then IN738LC alloy blade is reshaped, and the tensile property of reshaped area at room temperature after reshaping is 692MPa, which can only reach 65% of the strength of blade base material.

[0082] In summary, the remolding chamber of IN738LC alloy blade according to the scheme disclosed in Comparative Example 1-3 is weaker than the scheme disclosed in the embodiment in terms of tensile property at room temperature; thus, the activator provided in the embodiment does not add high concentration of B, Zr and Hf as melting point depressants, but realizes the melting point depression of the activator material by regulating the proportion of necessary alloying elements of the nickel-based superalloy, thereby avoiding the generation of boride brittle phase and low melting point eutectic phase rich in B, Zr and Hf in the heat preservation metallurgical process, which will significantly improve the high temperature mechanical properties of the remolding zone of IN738LC alloy blade.

[0083] The creep property test of the shape and property remolding zone and the blade substrate is carried out, and the test results are shown in Table 3.

[0084] Table 3: Creep property of shape and property remolding zone and substrate

[0085]

[0086] The macroscopic morphology of the microstructure of the shape and property remolding zone is shown in Figure 3 , the microstructure of the shape and property remolding zone is dense, the interface connection is good, and no large bulk of heterogeneous weakening phase is found; the microscopic morphology of the microstructure is shown in Figure 4 , the proportion of γ' strengthening phase in the shape and property remolding zone is high and the morphology is excellent. The average composition of main elements in the shape and property remolding zone and the substrate is analyzed by field emission scanning electron microscope EDS energy spectrum, and the results are shown in Table 4, the γ' phase generating elements Al+Ti+Ta+Nb in the shape and property remolding zone is about 10.7(wt%), the γ phase solid solution strengthening elements W+Mo+Ru in the shape and property remolding zone is about 5.1(wt%), the γ' phase generating elements Al+Ti+Ta+Nb in the substrate is about 9.7(wt%), the γ phase solid solution strengthening elements W+Mo in the substrate is about 4.2(wt%), and the content of main mechanical property strengthening elements in the shape and property remolding zone is very close to or slightly higher than that of the substrate.

[0087] Table 4: Comparison of average composition of main elements in shape and property remolding zone and substrate by EDS energy spectrum analysis

[0088]

[0089] The present application is not limited to the foregoing specific embodiments. The present application extends to any novel one, or any new combination, of the characteristics disclosed in this specification, as well as to any novel method or process disclosed in any step or any new combination.

Claims

1. An activator for reshaping blade damage defects, applied to IN738LC alloy blades, characterized by: The preparation of the activator includes at least the following elements in mass percentage: Cr: 16.1%-19.8%, Co: 9.2%-12.8%, Al: 1.2%-2.7%, Ti: 9.6%-11.7%, Nb: 5.6%-7.3%, Ru: 4.6%-5.8%, Mg: 0.005%-0.01%; the rest is Ni and unavoidable impurity elements; The melting temperature range of the activator is 1131°C-1160°C; The particle size of the activator is 23 μm-30 μm.

2. The activator according to claim 1, characterized in that The activator was prepared by a rotating electrode method.

3. A repair agent for reshaping blade damage defects, characterized in that: The invention comprises a curing agent, a binder and the activator according to any one of claims 1 to 2, wherein the activator, the curing agent and the binder are uniformly mixed in proportion.

4. The repairing agent according to claim 3, characterized in that The activator, curing agent and adhesive are evenly mixed in a mass ratio of 3:6:1; the curing agent is detitaniumized GTD111 commercial customized alloy powder, and the composition of GTD111 commercial customized alloy powder is: C: 0.1wt%, Cr: 14.0wt%, Co: 9.5wt%, Mo: 1.6wt%, W: 3.8wt%, Ta: 2.8wt%, Al: 3.0wt%, Zr: 0.02wt%, B: 0.012wt%, and the particle size is 75μm-150μm; the adhesive is a NICROBRAZS-BINDR type commercial adhesive.

5. A method for repairing blade damage defects and reshaping the blade, characterized in that: The following steps are involved: S1: preparing the repair agent according to any one of claims 3 to 4; S2: blade defect shaping; Applying the repair agent obtained in step S1 to the damaged defect of the nickel-based high-temperature alloy blade; S3: leaf shape remodeling; The blades that have completed step S2 are kept warm in a vacuum environment, and then cooled in the furnace. After cooling, the blades are heat treated and reshaped to complete the reshaping of the damage defects.

6. The repair method according to claim 5, characterized in that: In step S2, before applying the repair agent, the damaged defect needs to be cleaned in step S21; S21: Cleaning: Grind away the oxide layer at the damaged defect, then place the damaged defect in an alcohol or acetone solution for ultrasonic cleaning, and then dry at low temperature after cleaning.

7. The repair method according to claim 5, characterized in that: In step S3, the vacuum degree of the vacuum environment is better than 1x10 -3 Pa.

8. The repair method according to claim 5, characterized in that: In step S3, the holding temperature is 1190° C.-1220° C., and the holding time is 45 min-75 min.

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