Activators, repair agents and reshaping methods for leaf damage defect reshaping

Abstract

The application discloses an activator, a repairing agent and a reshaping method for blade damage defect shape and property, relates to the technical field of nickel-based high-temperature alloy repairing, and the preparation of the activator comprises the following elements with the mass percentage of Cr (10.2%-12.8%), Co (19.5%-24.8%), Al (1.2%-3.8%), W (7.8-10.7%), Hf (3.5%-5.5%), Ti (7.1%-9.9%), Ta (8.1%-10.9%), Ru (3.2%-5.8%) and Ce (0.005%-0.02%). The repairing agent comprises the activator, a curing agent and an adhesive which are mixed uniformly in proportion. The application avoids the performance decline of the blade substrate caused by heat treatment, improves the high-temperature mechanical properties and the high-temperature creep resistance of the repaired position of the blade, weakens the adverse effect of cold and hot fatigue on the shape and property reshaping area, and avoids the generation of more pores in the shape and property reshaping 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 reshaping method. BACKGROUND

[0002] Mar-M247 nickel-based superalloy was developed by Martin Corporation of the United States in the late 20th century. The nominal chemical composition of the equiaxed crystal alloy is:

[0003] Ni-8wt%Cr-10wt%Co-10wt%W-5.5wt%Al-1wt%Ti-3wt%Ta-1.5wt%Hf-0.6wt%Mo-0.15wt%C-0.015wt%B-0.03wt%Zr; has excellent castability and good creep resistance and hot corrosion resistance, and is widely used to manufacture aero-engine and heavy gas turbine turbine blades, and the working temperature can reach 1000°C. The intracrystalline of the alloy is strengthened by γ' phase with a volume fraction of up to 62%, and the grain boundary is strengthened by discontinuous granular carbide, γ' phase and γ+γ' eutectic phase.

[0004] Although the high volume fraction of γ' phase improves the high temperature mechanical properties of Mar-M247 alloy, it also leads to poor weldability. When using fusion welding to repair the damage defects (cracks, thinning, etc.) of the alloy blade, thermal cracks are extremely easy to produce, and the repair effect is very poor. In the field of nickel-based superalloy repair, powder metallurgy repair technology is particularly suitable for the repair and remanufacturing of high-aluminum and titanium-containing 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 sintered in a vacuum furnace, thereby realizing the shape and property reshaping of the damage area of the blade.

[0005] Patents CN114632990A, CN114703472A and CN114669738A respectively report several brazing repair materials for Mar-M247 alloy, and the room temperature tensile strength of the repaired joint can reach 80% of the base material (CN114703472A), but the above-mentioned materials still have some problems, the above-mentioned repair materials, although the high concentration of B (CN114703472A), Zr (CN114632990A) and Hf (CN114669738A) is introduced to achieve the melting point suppression effect of the solder, but also lead to the generation of a large number of boride brittle phases and B-rich, Zr-rich, Hf-rich eutectic phases and other harmful phases in the repair area, which will cause the following serious consequences: 1) The melting points of these harmful phases are mostly lower than the solid solution heat treatment temperature (about 1230℃) of Mar-M247 nickel-based high-temperature alloy blade, so the temperature needs to be reduced to prevent the remolded area from melting during the solid solution heat treatment of the remolded blade, which will cause part of the harmful phases in the blade matrix to not be remelted, and the best recovery heat treatment effect cannot be achieved; 2) The boride and B-rich, Zr-rich, 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 the high-temperature mechanical properties of the remolded area to be severely reduced, so it cannot be used for repairing blades in high-stress working conditions, and to some extent, it limits its application range; 3) The B in the remolded blade will diffuse to the coating during service, causing the coating of the blade to fail prematurely. SUMMARY

[0006] The purpose of the present application is to provide a kind of blade damage defect remolding activator, repair agent and remolding method for the above-mentioned problems, avoid the performance decline of blade matrix caused by heat treatment, improve the high-temperature mechanical properties and high-temperature creep resistance of the repaired position of the blade, weaken the adverse effects of cold and hot fatigue on the remolded area, and avoid the premature solidification of the capillary channel to cause a large number of pores in the remolded area.

[0007] The technical scheme adopted by the present application is as follows: a kind of blade damage defect remolding activator is applied to Mar-M247 alloy blade, and the preparation of the activator includes at least the following mass percentages of elements:

[0008] Cr (10.2%-12.8%), Co (19.5%-24.8%), Al (1.2%-3.8%), W (7.8-10.7%), Hf (3.5%-5.5%), Ti (7.1%-9.9%), Ta (8.1%-10.9%), Ru (3.2%-5.8%), Ce (0.005%-0.02%); the rest is Ni or / and unavoidable impurity elements.

[0009] Further, the activator can be prepared by the rotating electrode method.

[0010] Further, the melting temperature range of the activator is 1120-1150℃.

[0011] Further, the particle size of the activator is 30-53μm.

[0012] 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.

[0013] Further, the activator, the curing agent and the binder are mixed uniformly in proportion of 4:5:1 in mass ratio; the curing agent is a commercial alloy powder of M-21; and the binder is a commercial binder of NICROBRA S-BINDR type.

[0014] A reshaping method for reshaping of blade damage defect, comprising the following steps:

[0015] S1: preparing the repairing agent;

[0016] S2: shaping of blade defect;

[0017] applying the repairing agent obtained in step S1 to the damage defect of a Mar-M247 alloy blade;

[0018] S3: reshaping of blade shape;

[0019] performing heat preservation on the blade after step S2 in a vacuum environment, and after the heat preservation is completed, the blade is cooled down in the furnace, and after the cooling, the blade is heat treated and shaped, so that the reshaping of the damage defect is completed.

[0020] Further, in step S2, before the repairing agent is applied, the damage defect needs to be cleaned in step S21.

[0021] 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 the cleaning, the damage defect is dried at low temperature.

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

[0023] Further, in step S3, the heat preservation temperature is 1180-1200℃, and the heat preservation time is 60-120min.

[0024] According to the above technical scheme, the present application has the following advantages:

[0025] 1. The activator provided by the application 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 eutectic phases in the shape-property remodeling zone, which significantly improves the high-temperature mechanical properties of the blade repair joint;

[0026] 2. The shape-property remodeling zone obtained by the application is resistant to high temperatures (does not melt at 1230 DEG C), and thus can be subjected to performance recovery heat treatment at the standard heat treatment temperature of the Mar-M247 nickel-based high-temperature alloy blade, thereby effectively avoiding the performance degradation of the blade substrate caused by low recovery heat treatment temperatures;

[0027] 3. By adjusting the proportions of Co, Ti, Ta and Ru, the content of W can be increased to about 10% within a certain range, and the activator maintains a low melting point, thereby introducing W elements with the same content as the Mar-M247 alloy in a boron-free system while ensuring the processability of the activator, and significantly improving the high-temperature mechanical properties and high-temperature creep resistance of the shape-property remodeling zone;

[0028] 4. The introduction of Ru reduces the segregation concentration of TCP phase forming elements such as Co, Cr, Ti and W on the γ / γ' two-phase interface, effectively inhibits the precipitation behavior of TCP, significantly improves the microstructure stability of the metallurgical bonding zone, and, similar to the effect of W elements, allows the large-sized Ru elements with large atomic radii to be mainly solid-solved in the matrix γ phase, thereby significantly improving the high-temperature creep resistance of the alloy;

[0029] 5. The activator provided by the application and the M-21 commercial alloy powder solidifier can complement each other in terms of composition and process, so that the shape-property remodeling zone obtained is very close in composition to the substrate, which is beneficial to improve the quality uniformity of the repaired blade, ensures the dynamic balance thereof during service, and also ensures the matching of the thermal expansion coefficients of the shape-property remodeling zone and the substrate, thereby reducing the adverse effects of cold and hot fatigue on the shape-property remodeling zone;

[0030] 6. The activator powder provided by the application has a near-equal diameter, can realize near-isothermal melting during the holding stage, is beneficial to the filling of liquid phases between the solidifier powder and the substrate interface and the interstices between the solidifier powders, and can effectively avoid the premature solidification and closure of capillary channels to generate more pores in the shape-property remodeling zone. BRIEF DESCRIPTION OF DRAWINGS

[0031] The application will be described by way of example and with reference to the accompanying drawings, in which:

[0032] Figure 1 The DSC curve of the activator disclosed by the application;

[0033] Figure 2 The microstructure of the activator disclosed by the application;

[0034] Figure 3 The present application discloses the macroscopic morphology of the Mar-M247 high-temperature alloy after the shape and property are remodeled.

[0035] Figure 4 The present application discloses the microscopic morphology of the Mar-M247 high-temperature alloy after the shape and property are remodeled. DETAILED DESCRIPTION

[0036] All features disclosed in this specification, and / or all steps of any methods or processes disclosed in this specification, can be combined in any combination, except combinations where at least some of such features and / or steps are mutually exclusive.

[0037] Any of the features disclosed in this specification, unless explicitly stated otherwise, can be replaced by alternative features serving the same, or a similar, purpose.

[0038] Embodiment 1

[0039] As shown in Figures 1-2 An activator for remodeling the shape and property of a blade damage defect is applied to a Mar-M247 alloy blade, and the preparation of the activator includes at least the following elements with the mass percentage:

[0040] Cr (10.2%-12.8%), Co (19.5%-24.8%), Al (1.2%-3.8%), W (7.8-10.7%), Hf (3.5%-5.5%), Ti (7.1%-9.9%), Ta (8.1%-10.9%), Ru (3.2%-5.8%), Ce (0.005%-0.02%); the rest is Ni or / and unavoidable impurity elements.

[0041] In this embodiment, the activator disclosed in this embodiment is used for service defect remodeling of a Mar-M247 nickel-based high-temperature alloy blade, and several repair materials for repairing Mar-M247 alloy are also disclosed in patents CN114703472A, CN114632990A and CN114669738A, and the difference between the activator of the present application and the above-mentioned patents is that high-concentration B, Zr and Hf are not added as melting point inhibitors, which avoids the generation of boride brittle phase and low-melting eutectic phase rich in B, Zr and Hf in the shape and property remodeling area, and the organization and composition of the shape and property remodeling area obtained are close to the base material, which significantly improves the mechanical properties of the joint.

[0042] Based on the alloy composition of Mar-M247 alloy, the elements used in the activator of this embodiment include Cr, Co, Al, W, Hf, Ti, Ta, Ru and Ce, and the beneficial effects are as follows:

[0043] Cr is an indispensable alloying element in the alloy, most of which is dissolved in the γ phase, has a small solid solution strengthening effect, but can significantly improve the high temperature oxidation resistance and hot corrosion resistance of the shape and property remodeling area, and can form carbides that strengthen the grain boundary in combination with C. The content of Cr is limited to the range of 10.2wt% to 12.8wt% in the present application.

[0044] Co can be infinitely soluble with the base element Ni to form a continuous substitution solid solution, which has a solid solution strengthening effect on the matrix, can reduce the matrix stacking fault energy, and has a limited effect on the melting point of the alloy, but can significantly reduce the solid solution temperature of the γ' phase. The content of Co is limited to the range of 19.5wt% to 24.8wt% in the present application.

[0045] Al is the main generating element of the γ' phase, and the high temperature creep resistance of the shape and property remodeling area is proportional to the number of γ' phases in a unit volume to a certain 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 to the range of 1.2wt% to 3.8wt% in the present application, but this does not mean that the Al content of the finally obtained shape and property remodeling area will be lower than that of Mar-M247 alloy substrate (containing 5.5wt% of Al), it is emphasized that the activator in the present application is used in combination with the solidifying agent, and the missing Al can be supplemented by the M-21 commercial alloy powder (containing 6.0wt% of Al) matched therewith.

[0046] W is an important strengthening element of the γ phase in Mar-M247 alloy, with a mass fraction close to 10%, which has a significant solid solution strengthening effect, has an atomic radius much larger than Ni, and is dissolved in the matrix to cause obvious lattice expansion, increase 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. Due to its large atomic radius and slow diffusion rate, in order to make the W content of the shape and property remodeling area uniform and close to that of the substrate, the content of W in the present application is limited to the range of 7.8wt% to 10.7wt%.

[0047] Ti and Ta are both strengthening elements of the γ' phase in Mar-M247 alloy, which can change the composition of the γ' phase, increase the reverse domain boundary energy of the γ' phase, and improve the stability of the γ' phase. In the present application, Ti and Ta also act as melting point suppression elements, the content of Ti is limited to the range of 7.1wt% to 9.9wt%, and the content of Ta is limited to the range of 8.1wt% to 10.9wt%. Co, W, and Ru cooperate with each other to suppress the melting point of the alloy to the process range, it is emphasized that excessive Ti and Ta in the activator of the present application can be balanced by the M-21 commercial alloy solidifying agent powder (not containing Ti and Ta), so that the finally obtained shape and property remodeling area will not generate harmful phases due to the enrichment of Ti and Ta.

[0048] Hf is also one of the γ' phase strengthening elements, and can promote the generation of curved grain boundaries in the shape remodified zone, strengthen the grain boundaries, and improve the compatibility and adhesion of the coating and the shape remodified zone. In the present application, the content of Hf is limited to the range of 3.5 wt% to 5.5 wt%.

[0049] Ru is a rare earth element, and the purpose of adding it is to improve the microstructure stability of the shape remodified zone. In the present application, Ru also has the effect of weak melting point inhibition. In addition, the Ru element with a large atomic radius is mainly solid-solved in the matrix γ phase, which can significantly improve the high-temperature creep resistance of the alloy. In the present application, the content of Ru is limited to the range of 3.2 wt% to 5.8 wt%.

[0050] Ce is a rare earth element, and a small amount of addition can have the following beneficial effects: 1) desulfurization, reducing the harmful effects of sulfur on the grain boundaries; 2) as a micro-alloying element, it is segregated at the grain boundaries to strengthen the grain boundaries; 3) improving the surface stability of the shape remodified zone and improving the oxidation resistance. In the present application, the content of Ce is limited to the range of 0.005 wt% to 0.02 wt%.

[0051] Example 2

[0052] On the basis of Example 1, in order to further clearly illustrate and explain the technical solutions of the present application, the following non-limiting embodiments are provided. Table 1 is the embodiment of the present application, and the following element content data are mass percentage data.

[0053] Table 1 Embodiments of the activator

[0054]

[0055] In the embodiments 1-4 of the present application, the advantages are as follows:

[0056] 1. The activator provided by the present application does not add high concentrations of B, Zr, and Hf as melting point inhibitors, thereby avoiding the generation of boride brittle phases and B-rich, Zr-rich, and Hf-rich low-melting eutectic phases during the holding metallurgy process, which significantly improves the high-temperature tensile properties of the Mar-M247 alloy blade shape remodified zone.

[0057] 2. The activator provided by the present application contains a high concentration of solid-solution strengthening element W, so that the W element with a large atomic radius is mainly solid-solved in the matrix γ phase, which can significantly improve the high-temperature creep resistance of the alloy.

[0058] 3. The activator composition design provided by the present invention is based on the theory of high entropy alloying, and therefore contains relatively high concentrations of elements such as Ti, Ta, Co, and W. Although the clever combination with the M-21 type 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, the introduction of a certain amount of rare earth element Ru reduces the segregation concentration of TCP phase-forming elements such as Co, Cr, Ti, and W at the γ / γ' phase interface, effectively inhibits the precipitation behavior of TCP, significantly improves the structural stability of the metallurgical bonding zone, and, similar to the effect of W, can significantly improve the high-temperature creep resistance of the alloy.

[0059] 4. The high concentration of W element addition (including 10.0wt% W) is a major feature of the Mar-M247 alloy. W has a very high melting point (3400°C). Traditional activator composition design theory believes that introducing a large amount of W is detrimental to the melting point suppression effect of the activator. However, based on cluster bonding theory, the present invention finds that by adjusting the ratios between Co, Ti, Ta, and Ru, the W content can be increased to about 10% within a certain range while maintaining a low melting point of the activator. Introducing W elements at a content equivalent to that of the Mar-M247 alloy into a boron-free system ensures the processability of the activator while significantly improving the high-temperature mechanical properties and high-temperature creep resistance of the morphologically reshaped zone.

[0060] In a feasible embodiment, the activator can be prepared by a rotating electrode method; the rotating electrode method is known to those skilled in the art and will not be described in detail in this specification.

[0061] Furthermore, the melting temperature of the activator ranges from 1120°C to 1150°C.

[0062] like Figure 1 As shown, the DSC curve of the activator disclosed in embodiment 1 of this example.

[0063] Further, if Figure 2 As shown, the microscopic morphology of the activator disclosed in embodiment 1 of this embodiment has a particle size of 30μm-53μm, and its size is nearly equal to the diameter, which can achieve near-isothermal melting in the insulation stage, and is conducive to the nearly isochronous filling of the gaps between the interface of the curing agent powder and the substrate and between the curing agent powders by the liquid phase, which can effectively avoid the premature solidification and closure of the capillary channel, resulting in the generation of more pores in the shape reshaping zone.

[0064] The activator disclosed in this embodiment has a wide range of applicability. It can be used with the M-21 commercial curing agent to reshape the damaged defects of Mar-M247 alloy blades. Multiple parts can be repaired at one time with high repair efficiency and low cost, and has high industrial application value.

[0065] Example 3

[0066] A repair agent for reshaping of blade damage defect, comprising a curing agent, a binder and the activator as described in embodiment 1 of embodiment 2, the activator, the curing agent and the binder are mixed uniformly in proportion.

[0067] Specifically, the activator powder, the curing agent and the binder as described in embodiment 1 are mixed uniformly in a mass ratio of 4:5:1 to form a plastic shaping paste; the curing agent is selected from a commercially available alloy powder of M-21 type, and the composition is: C (0.13 wt%), B (0.02 wt%), Cr (5.7 wt%), Mo (2.0 wt%), Al (6.0 wt%), W (11.0 wt%), Nb (1.5 wt%), Zr (0.12 wt%), and the particle size is 75-150 μm; the binder is a commercially available binder of NICROBRAZ S-BINDR type.

[0068] It should be noted that the paste-shaped repair agent makes the repair agent viscous, reduces the flowability, makes the repair agent stable when filling the reshaping position, avoids the repair agent from leaving the reshaping position before entering the heating and melting; and the viscous repair agent is more convenient to fill the reshaping area, which specifically shows that the viscous repair agent has a certain flowability, and when the repair agent fills the reshaping 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 reshaping area, and completely fill the defect gap in the reshaping area under the action of its flowability.

[0069] In this embodiment, the repair agent is the activator and the M-21 commercially available alloy powder curing agent which can complement each other in composition and process, so that the reshaped area obtained is very close to the base material in composition, which is beneficial to improve the quality uniformity of the repaired blade, ensures the dynamic balance in the service process, and also ensures the matching of the thermal expansion coefficient of the reshaped area and the base material, reduces the adverse effects of cold and hot fatigue on the reshaped area.

[0070] Embodiment 4

[0071] A reshaping method for reshaping of blade damage defect, comprising the following steps:

[0072] S1: preparing the repair agent as described in embodiment 3.

[0073] S2: blade defect shaping; the damage defect of the Mar-M247 alloy blade needs to be cleaned and then coated with the repair agent; specifically as follows:

[0074] S21: removing the oxide layer on the defect surface of the Mar-M247 alloy blade with a hard alloy steel drill bit, the defect size is less than 40mm in length, 40mm in width and 5mm in height, and after polishing, the blade is placed in an alcohol or acetone solution for ultrasonic cleaning for 60 minutes and then dried for standby.

[0075] S22: applying the repair agent obtained in step S1 to the damaged defect of the Mar-M247 alloy blade;

[0076] S3: reshaping the blade;

[0077] In a vacuum environment with a vacuum degree better than 1x10 -3 Pa, the blade after step S2 is subjected to heat preservation at a temperature of 1210℃ for 80 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 reshaping to complete the reshaping of the damaged defect.

[0078] The reshaped area and the blade substrate are subjected to tensile test, and the test results are shown in Table 2.

[0079] Table 2: Tensile properties of the reshaped area and the substrate

[0080]

[0081] Therefore, using the activator described in embodiment 1 of example 2, combined with the solidifying agent and the adhesive, the damaged defect of the Mar-M247 alloy blade is reshaped, and the tensile strength of the reshaped area at room temperature is 917MPa, which can reach 93% of the strength of the blade substrate.

[0082] The following data is selected as a control example, as follows:

[0083] Control Example 1

[0084] Patent CN114703472A introduces a method for repairing nickel-based superalloy based on isothermal solidification principle, and in the embodiment, the powder with a composition of Ni-3wt.%Cr-5wt.%Co-4wt.%Al-1.5wt.%Ti-1.5wt.%Ta-4wt.%B and the powder with a composition of Ni-20at.%Cr-20at.%Co-16at.%Al-4at.%W-1.5at.%Ti-3.5at.%Ta are mixed in a mass ratio of 0.1:1 to reshape the Mar-M247 alloy blade, and the tensile property of the reshaped area at room temperature is 651MPa, which can only reach 80% of the strength of the blade substrate.

[0085] Control Example 2

[0086] Patent CN114632990A introduces a repair process for repairing defects of high-temperature alloy blades. In the examples, powders A and B with compositions of Ni-10wt.%Cr-10wt.%Co-4wt.%Al-4wt.%Ti-8wt.%Zr and Ni-15at.%Cr-18at.%Co-15at.%Al-5at.%W-4at.%Ti are mixed in a mass ratio of 0.2:1 to reshape the Mar-M247 alloy blade. The reshaped reshaped area has a room temperature tensile property of 542MPa, which can only reach 65% of the strength of the blade substrate.

[0087] Comparative Example 3

[0088] Patent CN114669738A introduces a repair material and a repair method for repairing gas turbine blades. In the examples, powders A and B with compositions of Ni-9wt.%Cr-12wt.%Co-4wt.%Al-2wt.%Ta-16wt.%Hf and Ni-15at.%Cr-20at.%Co-20at.%Al-6at.%W-1.8wt.%Ta are mixed in a mass ratio of 0.2:1 to reshape the Mar-M247 alloy blade. The reshaped reshaped area has a room temperature tensile property of 589MPa, which can only reach 70% of the strength of the blade substrate.

[0089] In summary, the schemes disclosed in Comparative Examples 1-3 have weaker room temperature tensile properties in the reshaped area after repairing Mar-M247 alloy blades than the scheme disclosed in the examples. Therefore, the activator provided by the present application does not add high concentrations of B, Zr, and Hf as melting point inhibitors, but controls the proportion of necessary alloying elements in the nickel-based high-temperature alloy to achieve the melting point inhibition effect of the activator material. Therefore, the formation of boride brittle phases and low-melting eutectic phases rich in B, Zr, and Hf during the heat preservation metallurgical process is avoided, which significantly improves the high-temperature mechanical properties of the reshaped area of the Mar-M247 alloy blade.

[0090] In the examples, the Mar-M247 alloy blade is repaired by the repair agent disclosed in the present application, and the reshaped area has high temperature resistance (does not melt at 1230℃). Therefore, performance recovery heat treatment can be performed at the standard heat treatment temperature of the Mar-M247 nickel-based high-temperature alloy blade, effectively avoiding the performance degradation of the blade substrate caused by low recovery heat treatment temperature.

[0091] The reshaped area and the blade substrate were subjected to creep property tests, and the test results are shown in Table 3.

[0092] Table 3 Creep properties of the reshaped area and the substrate

[0093]

[0094] The analysis of the microstructure of the shape and property remolding zone shows that the macrostructure morphology is as shown in Figure 3 The microstructure morphology is as shown in Figure 4 The microstructure morphology is as shown in

[0095] Table 4 Comparison of average composition of main elements in the shape and property remolding zone and the base material by EDS energy spectrum analysis

[0096]

[0097] 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 features disclosed in this specification, and to any novel method or process disclosed, or any novel combination of steps of the disclosed methods or processes.

Claims

1. An activator for reshaping blade damage defects, applied to Mar-M247 alloy blades, characterized by: The preparation of the activator includes at least the following elements in mass percentage: Cr: 10.2%-12.8%, Co: 19.5%-24.8%, Al: 1.2%-3.8%, W: 7.8%-10.7%, Hf: 3.5%-5.5%, Ti: 7.1%-9.9%, Ta: 8.1%-10.9%, Ru: 3.2%-5.8%, Ce: 0.005%-0.02%; the rest is Ni and unavoidable impurity elements; The melting temperature range of the activator is 1120℃-1150℃; The particle size of the activator is 30 μm to 53 μm.

2. The activator according to claim 1, characterized in that The activator can be 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 uniformly mixed in a mass ratio of 4:5:1; the curing agent is M-21 commercial alloy powder, and the composition of the M-21 commercial alloy powder is: C: 0.13wt%, B: 0.02wt%, Cr: 5.7wt%, Mo: 2.0wt%, Al: 6.0wt%, W: 11.0wt%, Nb: 1.5wt%, Zr: 0.12wt%, and the particle size is 75μm-150μm; the adhesive is NICROBRAZ S-BINDR commercial adhesive.

5. A method for reshaping blade damage defects, characterized in that: The following steps are involved: S1: preparing the repair agent according to any one of claims 3-4; S2: blade defect shaping; Applying the repair agent obtained in step S1 to the damaged defect of the Mar-M247 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 remodeling 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 remodeling 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 remodeling method according to claim 5, characterized in that: In step S3, the holding temperature is 1180° C.-1200° C., and the holding time is 60 min-120 min.

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