Activating agent, repairing agent and repairing method for blade damage defects for shape and performance restoration

Abstract

The present invention relates to the technical field of nickel-based high-temperature alloy restoration. Disclosed are an activating agent, repairing agent and repairing method for blade damage defects for shape and performance restoration. The activating agent at least comprises the following elements in percentage by mass: 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%) and Mg (0.005%-0.01%). The repairing agent comprises an activating agent, a curing agent, and an adhesive which are uniformly mixed at a ratio. According to the present invention, the creep resistance and mechanical properties of an alloy at high temperature can be effectively improved, and generation of a large amount of pores in a shape and performance restoration area caused by a capillary channel being solidified and closed in advance can be effectively prevented.

Description

Activator, repair agent and repair method for reshaping blade damage defects Technical Field

[0001] The present invention relates to the technical field of nickel-based high-temperature alloy repair, in particular to an activator, a repair agent and a repair method for reshaping blade damage defects. Background Art

[0002] The nickel-based superalloy Inconel 738LC (IN738LC) is a γ'-phase precipitation-strengthened alloy with an equiaxed 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. This alloy exhibits excellent structural stability and casting performance, operating at temperatures below 900°C. It is suitable for the production of precision-cast blades for aircraft engines and gas turbines. During service, turbine blades are subject to surface damage caused by long-term high-temperature gas corrosion, erosion, and thermal fatigue. Using effective repair methods to repair damaged areas can effectively extend blade service life and reduce maintenance costs.

[0003] For Inconel738LC nickel-based high-temperature alloy blades with high Al and Ti contents, conventional fusion welding repairs can easily cause cracking of the base material. In the field of nickel-based high-temperature alloy repair, powder metallurgy technology is particularly suitable for the repair and remanufacturing of cast high-temperature alloys with high aluminum and titanium contents. This technology is based on the principle of isothermal solidification and can effectively avoid the generation of thermal cracks in the repair area. It has many advantages such as low cost and high efficiency. The repair material used is a mixture of a low-melting-point activator that acts as a brazing agent and a high-melting-point curing agent that acts as a filler. A binder is added to form a paste that is applied to the surface of the workpiece and metallurgically sintered in a vacuum furnace to achieve the reshaping of the damaged area.

[0004] Patents CN114669820A, CN114632991A, and CN114669956A report on several powder metallurgy repair materials for IN738 alloy, achieving room-temperature tensile strengths of up to 723 MPa for the repaired joints. To ensure complete liquefaction of the solder at temperatures below the initial melting point of the substrate, these materials incorporate high concentrations of boron (CN114669820A), zirconium (CN114669956A), and hydrogen (CN114632991A) to suppress the solder's melting point. Although the processability of the solder is guaranteed, it also leads to significant differences in the elemental composition and microstructure between the solder and the substrate. The resulting reshaped zone will produce a large number of boride brittle phases and low-melting-point eutectic phases rich in B, Zr, and Hf. This will have the following consequences: 1) These low-melting-point harmful phases will melt during the solution heat treatment (approximately 1130°C) of the IN738LC nickel-based superalloy blade. To prevent the reshaped zone from remelting during the solution heat treatment, the solution heat treatment temperature needs to be lowered. This will prevent the blade substrate from achieving the optimal recovery heat treatment effect, resulting in a decrease in the mechanical properties of the substrate; 2) Borides and eutectic phases rich in B, Zr, and Hf are brittle phases and difficult to eliminate through heat treatment. Large pieces of precipitation and connection into sheets will cause a serious decline in the high-temperature mechanical properties of the reshaped zone, making it unsuitable for repair work on blades under high stress conditions, which to a certain extent limits its application range; 3) During service, the B in the reshaped zone of blades repaired with B-rich repair materials will diffuse into the coating, causing premature failure of the blade coating.

[0005] Summary of the Invention

[0006] The purpose of the present invention is to provide an activator, a repair agent and a repair method for the reshaping of blade damage defects in response to the above-mentioned problems, which can effectively improve the creep resistance and mechanical properties of the alloy at high temperatures, and effectively avoid the premature solidification and closure of capillary channels, resulting in the formation of more pores in the reshaping area.

[0007] The technical solution adopted by the present invention is as follows: an activator for reshaping blade damage defects is applied to nickel-based high-temperature alloy blades. The preparation of the activator includes at least the following elements in mass percentage:

[0008] 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.

[0009] Furthermore, the activator is prepared by a rotating electrode method.

[0010] Furthermore, the melting temperature of the activator ranges from 1131°C to 1160°C.

[0011] Furthermore, the particle size of the activator is 23 μm-30 μm.

[0012] A repair agent for reshaping blade damage defects comprises a curing agent, a binder and the activator according to any one of claims 1 to 4, wherein the activator, curing agent and binder are uniformly mixed in proportion.

[0013] Furthermore, 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 adhesive is a NICROBRAZS-BINDR commercial adhesive.

[0014] A method for repairing blade damage defects and reshaping the blade, comprising the following steps:

[0015] S1: preparing the repair agent;

[0016] S2: blade defect shaping;

[0017] Applying the repairing agent obtained in step S1 to the damaged defect of the nickel-based high-temperature alloy blade;

[0018] S3: leaf shape remodeling;

[0019] 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.

[0020] Furthermore, in step S2, before applying the repair agent, the damaged defect needs to be cleaned in step S21;

[0021] 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.

[0022] Furthermore, in step S3, the vacuum degree of the vacuum environment is better than 1x10 -3 Pa;

[0023] Furthermore, in step S3, the holding temperature is 1190° C.-1220° C., and the holding time is 45 min-75 min.

[0024] In summary, due to the adoption of the above technical solution, the beneficial effects of the present invention are:

[0025] 1. The activator provided by the present invention does not add melting point depressants such as B, Zr, and Hf. Instead, it achieves melting point suppression of the activator material by regulating the proportions of essential alloying elements in the nickel-based high-temperature alloy. This effectively avoids the formation of brittle boride phases and low-melting-point eutectic phases such as B-rich, Zr-rich, and Hf-rich phases, and can significantly improve the high-temperature mechanical properties of the IN738LC alloy blade reshaping zone.

[0026] 2. The repair agent provided by the present invention cleverly combines an activator with a selected curing agent. The content of solid solution strengthening elements and γ' phase in the obtained reshaped zone is close to that of the substrate. This makes the microstructure of the obtained reshaped zone basically consistent with that of the substrate, and can significantly improve the high-temperature mechanical properties of the reshaped zone.

[0027] 3. The activator provided by the present invention introduces Ru to reduce the segregation concentration of TCP phase-forming elements such as Co, Cr, Ti, and Nb at the γ / γ' phase interface, effectively inhibiting the precipitation behavior of TCP and significantly improving the structural stability of the metallurgical bonding zone. In addition, Ru has a similar effect to W. The large-sized atomic radius of Ru is mainly dissolved in the matrix γ phase, which can significantly improve the high-temperature creep resistance of the alloy.

[0028] 4. The activator powder provided by the present invention has a size of nearly equal diameter, which can achieve nearly isothermal and isochronous melting in the insulation stage, which is conducive to the liquid phase filling the gaps between the interface between the curing agent powder and the substrate and between the curing agent powders, and can effectively avoid the premature solidification and closure of the capillary channel, resulting in the generation of more pores in the shape reshaping area. BRIEF DESCRIPTION OF THE DRAWINGS

[0029] The present invention will now be described by way of example with reference to the accompanying drawings, in which:

[0030] FIG1 is a DSC curve of the activator disclosed in the present invention;

[0031] FIG2 is a microscopic morphology of the activator disclosed in the present invention;

[0032] FIG3 shows the macroscopic structure of the IN738LC superalloy after shape reshaping disclosed in the present invention;

[0033] FIG4 shows the microstructure morphology of the IN738LC high-temperature alloy after shape reshaping disclosed in the present invention. DETAILED DESCRIPTION

[0034] All features disclosed in this specification, or all steps in the disclosed methods or processes, except mutually exclusive features and / or steps, can be combined in any manner.

[0035] 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.

[0036] Example 1

[0037] As shown in Figures 1 and 2, 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:

[0038] 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.

[0039] 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.

[0040] 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:

[0041] Cr is an important alloying element in IN738LC alloy, with a content of up to 16wt%. Its main function is to improve the high-temperature oxidation resistance and hot corrosion resistance of the alloy. 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%.

[0042] 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%.

[0043] Al is the primary element that generates the γ' phase. To a certain extent, the high-temperature creep resistance of the reshaping zone is proportional to the amount of γ' phase per unit volume. However, adding a large amount of Al will cause the melting point of the activator to rise sharply. Therefore, the present invention limits the Al content to a range of 1.2 wt% to 2.7 wt%. However, this does not mean that the γ' phase content in the final reshaping zone will be lower than that of the IN738LC alloy substrate. It should be emphasized that the activator of the present invention contains high concentrations of Ti and Nb elements, which will enter the γ' phase and replace a portion of Al, thereby increasing the volume percentage of the γ' phase.

[0044] In the IN738LC alloy, Ti and Nb are both γ'-strengthening elements, altering the γ' phase's composition, increasing its reverse domain boundary energy, and enhancing its high-temperature stability, correspondingly improving the strength and creep resistance of the reshaping zone. In the present invention, Ti and Nb serve as primary melting point-depressing elements, with Ti content limited to 9.6wt% to 11.7wt% and Nb content limited to 5.6wt% to 7.3wt%. Together, they work together with other alloying elements to suppress the alloy's melting point within the process range. It is important to note that the excess Ti and Nb in the present activator can be balanced by elemental diffusion-de-titaniumized GTD111 curing agent powder (which does not contain Ti and Ta), ensuring that the resulting reshaping zone does not exhibit the formation of deleterious phases due to Ti and Nb enrichment.

[0045] Ru is a rare earth element added to improve the structural stability of the reshaped zone. Another benefit of this invention is a weak melting point suppression effect. Simultaneously, Ru, with its large atomic radius, dissolves in the matrix's γ phase, causing lattice expansion and increasing the long-range elastic stress field. This hinders dislocation motion and reduces the elastic stress field, significantly improving the alloy's high-temperature creep resistance. The Ru content in this invention is limited to 4.6% to 5.8% by weight.

[0046] Mg is a microalloying element. Its trace addition balances segregation at grain boundaries, reduces grain boundary energy, and improves and refines the morphology of grain boundary carbides and other precipitated phases. It combines with the harmful impurity element S to form the high-melting-point compound MgS, which mitigates the harmful effects of S, purifies grain boundaries, enhances grain boundary cohesion, and increases grain boundary strength, effectively improving tensile shaping and durability in the reshaped zone. The Mg content in the present invention is limited to 0.005 wt% to 0.01 wt%.

[0047] Example 2

[0048] On the basis of Example 1, in order to further clearly illustrate and describe the technical solution of the present invention, the following non-limiting embodiments are provided. Table 1 shows the embodiments and comparative examples of the activator, and the following element content data are all mass percentage data.

[0049] Table 1 Implementation methods and comparison examples of activators

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

[0051] 1. The activator provided by the present invention does not add high concentrations of B, Zr, and Hf as melting point depressants. Instead, it achieves the melting point suppression effect of the activator material by regulating the proportions of the essential alloying elements of the nickel-based high-temperature alloy. Therefore, the formation of boride brittle phases and B-rich, Zr-rich, and Hf-rich low-melting-point eutectic phases during the heat-insulating metallurgical process is avoided. This will significantly improve the high-temperature mechanical properties of the IN738LC alloy blade reshaping zone.

[0052] 2. The activator composition design provided by the present invention is based on the high entropy alloying theory, and therefore contains relatively high concentrations of the elements Cr, Co, Ti, and Nb. Although the clever combination of the de-titaniumized GTD111 curing agent can balance the element concentrations in the entire morphological reshaping zone, the structural stability is low during the metallurgical bonding process, and the TCP phase has a high tendency to precipitate at high temperatures. Therefore, a certain amount of rare earth element Ru is introduced into the activator to reduce the segregation concentration of TCP phase-forming elements such as Co, Cr, Ti, and Nb at the γ / γ' phase interface, effectively inhibiting the precipitation behavior of TCP and significantly improving the structural stability of the morphological reshaping zone; at the same time, the Ru element with a large atomic radius is dissolved in the matrix γ phase, causing the matrix lattice expansion, increasing the long-range elastic stress field, thereby hindering dislocation movement and reducing the elastic stress field, which can significantly improve the high-temperature creep resistance of the alloy.

[0053] In a feasible implementation manner, the activator can be prepared by a rotating electrode method. The rotating electrode method is well known to those skilled in the art, and the specific process will not be described in detail in this specification.

[0054] In a feasible implementation manner, the melting temperature range of the activator is 1132°C-1160°C.

[0055] As shown in FIG1 , it is the DSC curve of the activator disclosed in embodiment 1 of this example.

[0056] A feasible implementation method is shown in Figure 2, which is the microscopic morphology of the activator disclosed in implementation method 1 of this embodiment. The particle size of the activator is 23μm-30μm, and its size is nearly equal to the diameter, which can achieve near-isothermal and isochronous melting in the insulation stage, which is conducive to liquid phase filling of the gaps between the interface of the curing agent powder and the substrate and between the curing agent powders, and can effectively avoid the premature solidification and closure of the capillary channel, resulting in the generation of more pores in the shape reshaping area.

[0057] The activator disclosed in this embodiment has a wide range of applicability. When used with GTD111 commercial customized alloy powder, the damage defects of IN738LC alloy blades are reshaped. The content of solid solution strengthening elements and γ' phase in the reshaped zone obtained is close to that of the substrate. This will make the microstructure of the reshaped zone basically consistent with that of the substrate, and can significantly improve the high-temperature mechanical properties of the reshaped zone. Multiple parts and multiple blades can be reshaped at one time, with high reshaping efficiency and low cost, and it has high industrial application value.

[0058] Example 3

[0059] A repair agent for reshaping blade damage defects comprises a curing agent, a binder and the activator described in Implementation Method 1 of Example 2, wherein the activator, curing agent and binder are uniformly mixed in proportion.

[0060] Specifically, the activator powder, curing agent, and adhesive described in Implementation Example 1 are mixed evenly in a mass ratio of 3:6:1 to form a shaping paste; the curing agent is a detitaniumized GTD111 commercial customized alloy powder, the composition of which 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%), with a particle size of 75μm-150μm; the adhesive is a commercial brand NICROBRAZ S-BINDR type adhesive.

[0061] It should be noted that the paste-like repair agent makes the repair agent viscous, reduces fluidity, and makes the repair agent stable when applied to the reshaped position, avoiding the repair agent from leaving the reshaped position before being heated and melted; and the viscous repair agent is more convenient for filling the reshaped area. Specifically, the viscosity has a certain fluidity. When the repair agent fills the reshaped position, the repair agent can change its own shape according to the size of the filling position due to its fluidity, meet the filling of irregular reshaped areas, and can be completely filled under the action of its own fluidity, reducing the defects and gaps in the reshaped area.

[0062] In this embodiment, the repair agent is a clever combination of an activator and a selected curing agent. The content of solid solution strengthening elements and γ' phase in the obtained morphologically reshaped zone is close to that of the substrate, which will make the organizational morphology of the obtained morphologically reshaped zone basically consistent with that of the substrate, and can significantly improve the high-temperature mechanical properties of the morphologically reshaped zone.

[0063] Example 4

[0064] A method for repairing blade damage defects and reshaping the blade, comprising the following steps:

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

[0066] S2: Blade defect shaping: The damaged defect of the IN738LC alloy blade needs to be cleaned and then coated with a repair agent; the details are as follows:

[0067] S21: Use a carbide steel drill to remove the oxide layer on the defective surface of the IN738LC alloy blade. The defect size is less than 40 mm long × 40 mm wide × 5 mm high. After grinding, place it in an alcohol or acetone solution for ultrasonic cleaning for 60 minutes, remove it and dry it for later use.

[0068] S22: applying the repair agent obtained in step S1 to the damaged defect of the IN738LC alloy blade;

[0069] S3: leaf shape remodeling;

[0070] The vacuum degree is better than 1x10 -3 The blades that have completed step S2 are kept warm in a vacuum environment of Pa, with a holding temperature of 1210°C and a holding time of 60 minutes. The vacuum environment can be provided by a vacuum furnace. After the insulation is completed, the blades are cooled in the furnace. After cooling, the blades are subjected to performance recovery heat treatment and reshaping to complete the shape reshaping of the damage defects.

[0071] The reshaped area and the blade substrate were subjected to tensile tests, and the test results are shown in Table 2.

[0072] Table 2 Tensile properties of the reshaped area and substrate

[0073] It can be seen that by using the activator described in embodiment 1 disclosed in Example 2, in combination with a curing agent and an adhesive to reshape the damage defects of the IN738LC alloy blade, the tensile strength of the reshaped area after reshaping is 864 MPa at room temperature, which can reach 87% of the strength of the blade substrate.

[0074] The following data are selected as a comparison example, the details are as follows:

[0075] Comparative Example 1

[0076] Patent CN114669820A introduces a repair agent and reshaping process for high-temperature alloy blades. In the embodiment, powder A with a composition 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 powder B with a composition of Ni-25at.%Cr-20at.%Co-20at.%Al-5at.%W-5at.%Mo-5at.%Ta-2at.%Nb-5at.%Ti are mixed in a mass ratio of 0.3:1 and then reshaped to IN738LC alloy blades. The room temperature tensile strength of the reshaped area after reshaping is 723MPa, which can only reach 70% of the strength of the blade substrate.

[0077] Comparative Example 2

[0078] Patent CN114632991A introduces a repair process for gas turbine blades based on powder metallurgy. In the embodiment, a low-melting-point powder containing Hf with a composition 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 a metal powder of a multi-principal alloy with a composition of Ni-20at.% Cr-20at.% Co-20at.% Al-5at.% W-5at.% Mo-5at.% Ta-2at.% Nb-5at.% Ti are mixed in a mass ratio of 0.1:1 and then the IN738LC alloy blade is reshaped. The room temperature tensile strength of the reshaped area after reshaping is 683 MPa, which can only reach 65% of the strength of the blade substrate.

[0079] Comparative Example 3

[0080] Patent CN114669956A introduces a powder metallurgy repair method for repairing defects in high-temperature alloy blades. In the embodiment, powder A with a composition of Ni-12wt.%Cr-5wt.%Co-2wt.%Al-3wt.%Ti-2wt.%W-2wt.%Mo-10wt.%Zr and powder B with a composition of Ni-18at.%Cr-18at.%Co-6at.%Al-2at.%W-2at.%Mo-2at.%Ti are mixed in a mass ratio of 0.15:1 and then the IN738LC alloy blade is reshaped. The room temperature tensile strength of the reshaped area after reshaping is 692MPa, which can only reach 65% of the strength of the blade substrate.

[0081] In summary, after the IN738LC alloy blade is reshaped, the room temperature tensile properties of the reshaped area of ​​the schemes disclosed in Control Examples 1-3 are weaker than those of the scheme disclosed in this embodiment; therefore, the activator provided by the present invention does not add high concentrations of B, Zr, and Hf as melting point inhibitors, but instead achieves the melting point inhibition effect on the activator material by regulating the proportion of necessary alloying elements of the nickel-based high-temperature alloy, thereby avoiding the formation of boride brittle phases and B-rich, Zr-rich, and Hf-rich low-melting point eutectic phases during the insulation metallurgy process, which will significantly improve the high-temperature mechanical properties of the morphological reshaped area of ​​the IN738LC alloy blade.

[0082] The creep performance test of the reshaped area and the blade substrate was carried out, and the test results are shown in Table 3.

[0083] Table 3 Creep properties of the morphological remodeling zone and substrate

[0084] The microstructure of the reshaped zone was analyzed. The macroscopic morphology is shown in Figure 3. The reshaped zone has a dense structure, good interface connectivity, and no large heterogeneous weakening phases are observed. The microscopic morphology is shown in Figure 4. The reshaped zone has a high proportion of γ' strengthening phase and excellent morphology. Field emission scanning electron microscopy (EDS) spectroscopy was used to analyze the average composition of the main elements in the reshaped zone and the base material. The results are shown in Table 4. The γ'-forming elements Al+Ti+Ta+Nb in the reshaped zone are approximately 10.7 wt%, and the solid solution strengthening elements W+Mo+Ru in the reshaped zone are approximately 5.1 wt%. The γ'-forming elements Al+Ti+Ta+Nb in the base material are approximately 9.7 wt%, and the solid solution strengthening elements W+Mo in the base material are approximately 4.2 wt%. The content of the main mechanical property-strengthening elements in the reshaped zone is very close to or slightly higher than that in the base material.

[0085] Table 4 Comparison of the average composition of the main elements in the morphologically reshaped area and the base material by EDS analysis

[0086] The present invention is not limited to the aforementioned specific embodiments, but extends to any new features or any new combination disclosed in this specification, as well as any new method or process steps or any new combination disclosed.

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 / or unavoidable impurity elements.

2. The activator according to claim 1, characterized in that: The preparation of the activator includes at least the following elements in mass percentage: Cr (19.8%), Co (9.2%), Al (2.7%), Ti (11.7%), Nb (6.5%), Ru (4.6%), Mg (0.005%); the rest is Ni and / or inevitable impurity elements.

3. The activator according to claim 1, characterized in that: The preparation of the activator includes at least the following elements in mass percentage: Cr (17.3%), Co (11.3%), Al (2.5%), Ti (10.7%), Nb (7.3%), Ru (5.8%), Mg (0.006%); the rest is Ni and / or inevitable impurity elements.

4. The activator according to claim 1, characterized in that: The preparation of the activator includes at least the following elements in mass percentage: Cr (18.8%), Co (12.8%), Al (1.2%), Ti (9.6%), Nb (5.6%), Ru (4.9%), Mg (0.01%); the rest is Ni and / or inevitable impurity elements.

5. The activator according to claim 1, characterized in that: The preparation of the activator includes at least the following elements in mass percentage: Cr (16.1%), Co (10.8%), Al (1.9%), Ti (10.5%), Nb (5.8%), Ru (5.3%), Mg (0.008%); the rest is Ni and / or inevitable impurity elements.

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

7. The activator according to claim 1, characterized in that: The melting temperature of the activator ranges from 1131°C to 1160°C.

8. The activator according to claim 1, characterized in that: The particle size of the activator is 23 μm-30 μm.

9. A repairing agent for reshaping blade damage defects, characterized in that: The invention comprises a curing agent, a bonding agent and the activator according to any one of claims 1 to 8, wherein the activator, the curing agent and the bonding agent are uniformly mixed in proportion.

10. The repairing agent according to claim 9, characterized in that: The activator, curing agent and adhesive are uniformly mixed in a mass ratio of 3:6:1; the curing agent is de-titaniumized GTD111 commercial customized alloy powder; and the adhesive is a NICROBRAZS-BINDR commercial adhesive.

11. 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 9 to 10; 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 damaged defects.

12. The repair method according to claim 11, characterized in that: In step S2, before applying the repair agent, the damaged defect needs to be cleaned in step S21; S21: Cleaning: Grind out the oxide layer at the damaged defect, then place the damaged defect in alcohol or acetone solution for ultrasonic cleaning, and then dry at low temperature after cleaning.

13. The repair method according to claim 11, characterized in that: In step S3, the vacuum degree of the vacuum environment is better than 1x10 -3 Pa.

14. The repair method according to claim 11, characterized in that: In step S3, the insulation temperature is 1190° C.-1220° C., and the insulation time is 45 min-75 min.

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