CN115927917A - high-W, mo-content nickel-based superalloy powder and application thereof, repairing agent and preparation thereof, and alloy repairing method - Google Patents
high-W, mo-content nickel-based superalloy powder and application thereof, repairing agent and preparation thereof, and alloy repairing method Download PDFInfo
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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Abstract
The invention discloses nickel-based superalloy powder with high W, mo content, application thereof, a repairing agent, preparation thereof and an alloy repairing method, wherein the preparation of the alloy powder needs elements and corresponding mass percentages as follows: c (0.05% -0.20%), cr (15.00% -20.00%), co (8.00% -12.00%), W (8.00% -12.00%), mo (10.00% -15.00%), ta (1.00% -5.00%), al (4.00% -6.00%), ti (4.00% -6.00%), nb (0-0.60%); the repair agent comprises 50-70% of alloy powder, 25-45% of B-containing activation assistant and 5% of binder by mass percent. The invention can stabilize the B element in the low-melting-point B-containing activation auxiliary agent, effectively weaken the adverse effect of high-concentration B in the repaired joint on the joint performance, obviously improve the durability and the oxidation resistance of the repaired area, enable the metallographic structure characteristics of the repaired area to be basically consistent with those of the nickel-based superalloy casting, and ensure the mechanical property and the material property of the repaired nickel-based superalloy casting in the repaired area.
Description
Technical Field
The invention relates to the field of alloy repair materials, in particular to nickel-based high-temperature alloy powder with high W, mo content, application thereof, a repair agent, preparation thereof and an alloy repair method.
Background
In the service process of hot-cast forged components such as turbine rotor blades, guide vanes and the like of industrial gas turbines, mechanical fatigue cracks, surface abrasion, oxidation corrosion, foreign object damage and other geometric structure defects appear on the surfaces of the components due to the action of long-term high-temperature and high-pressure gas. These defects, if left untreated, create a risk to the safe operation of the plant. Because the high-temperature alloy contains various noble metal elements, the production and manufacturing cost is higher, if the damaged workpiece is directly replaced, the maintenance cost of the unit is greatly increased, and the operation and maintenance cost of the unit can be effectively reduced by repairing the damaged area of the workpiece through an effective repairing technology. However, the high-temperature alloy as a precipitation hardening nickel-based high-temperature alloy has poor weldability, and cannot repair damaged areas in a common welding mode.
The powder metallurgy additive repair is an advanced repair technology for hot end components of aero-engines and ground combustion engines, and is particularly suitable for repairing and remanufacturing cast high-temperature alloy hot end components with high aluminum and titanium contents. The main current repair material is a low melting point activation adjuvant and a high melting point plastic powder. Among them, the design of the low melting point activation assistant which occupies a relatively small amount has been studied so far, and the low melting point activation assistant which has been widely reported and used is mostly based on N i and Co, with B added in excess as a melting-reducing element, and with Ta, A l, T i, W, cr added in an appropriate amount as a reinforcing element. For example, the commercial designations AMDRYDF-3 (N i-20Cr-20Co-3Ta-3B-0.02 La), NB171 (N i-10Cr-3.5Si-3.5 Fe-2.5B-12W), NB200 (Ni-7 Cr-6W-4.5Si-3.2 Fe-3.2B-0.06C), AMS4783 (Co-8 Si-19Cr-17 Ni-4W-0.8B), AMDRYDF-4B (Ni-14 Cr-10Co-3.5Al-2.5 Ta-2.7B-0.05Y), and the like, as well as some published patents on structural brazing alloys for superalloy components, such as CN1056645A, CN1800425A, CN101306494A, CN101780610A, CN101780604A, CN101780612A, CN103894599B, CN109909641A, and the like. The high melting point plastic powder with more usage is generally made of high temperature alloy with the same grade as the base material.
In the powder metallurgy repair process, the low-melting-point B-containing activation auxiliary agent is firstly liquefied at high temperature, B in a liquid phase is combined with Cr, mo and W elements in the activation auxiliary agent to generate massive boride, the rest B is combined with Cr, mo and W elements in the high-melting-point plastic powder, the content of B in the liquid phase is reduced, the melting point is increased, isothermal solidification is carried out on a repair area, and a repair joint with high strength is formed. If the content of Cr, mo and W elements in the repair area is not enough to combine with all free B, a part of liquid phase cannot be solidified isothermally, and eutectic with low melting point is formed and exists in the repair area when the liquid phase is cooled. Joints repaired by this technique, while able to withstand higher service temperatures, still face a number of problems: first, the bulk boride and low melting eutectic phase are hard brittle phases, and their presence in large amounts in the repair zone can result in a severe reduction in tensile properties of the joint. Secondly, in the nickel-based high-temperature alloy, mo and W are important solid solution strengthening elements of a gamma phase, cr is one of the most main elements for improving the oxidation resistance and the hot corrosion resistance of the repaired joint, and a large amount of Cr, mo and W are combined with B to generate boride, so that the elements lose the original strengthening effect, and the durability and the oxidation resistance of the joint in a repaired area are seriously reduced. Thirdly, the concentrations of Cr, mo and W in a gamma phase of a repair area are seriously reduced, and the Kendall effect can promote strengthening elements such as Cr, mo and W in the parent metal to diffuse to the repair area during high-temperature service, so that deeper parent metal tissues are changed, and the properties of the parent metal are deteriorated.
At present, for a repair material used in the powder metallurgy additive repair of a nickel-based superalloy casting, component design is mostly concentrated on a low-melting-point B-containing activation auxiliary agent with a small dosage, targeted component design is not carried out on high-melting-point plastic powder with a large dosage, and mature commercial superalloy powder is mostly used, which cannot effectively weaken the adverse effect of high-concentration B on the joint performance of a repair joint.
Disclosure of Invention
One object of the present invention is: aiming at the existing problems, the nickel-based superalloy powder with the high W, mo content and the application thereof, the repairing agent and the preparation method thereof and the alloy repairing method thereof are provided, the B element in the B-containing activation auxiliary agent with the low melting point can be stabilized, the adverse effect of the high-concentration B in the repaired joint on the joint performance can be effectively weakened, the durability and the oxidation resistance of a repaired area are obviously improved, the metallographic structure characteristics of the repaired area can be basically consistent with those of a nickel-based superalloy casting by adjusting the proportion of corresponding elements, and the mechanical property and the material property of the repaired nickel-based superalloy casting in the repaired area are ensured.
The technical scheme adopted by the invention is as follows: the nickel-based high-temperature alloy powder with the high W, mo content at least comprises the following elements in percentage by mass:
C(0.05％-0.20％)，Cr(15.00％-20.00％)，Co(8.00％-12.00％)，W(8.00％-12.00％)，Mo(10.00％-15.00％)，Ta(1.00％-5.00％)，Al(4.00％-6.00％)，Ti(4.00％-6.00％)，Nb(0-0.60％)。
further, the balance is Ni or/and unavoidable impurity elements.
Furthermore, the content of Cr, co, ta, al, ti and Nb in the alloy powder can be adjusted according to the components of the repaired base material; the contents of Mo and W can be adjusted according to the dosage of the low-melting-point B-containing activation assistant and the components of the repair base material.
Further, the melting temperature of the alloy powder ranges from 1250 ℃ to 1300 ℃.
Further, the particle size of the alloy powder is 30 μm to 106 μm.
The alloy powder is applied to the repair of the nickel-based high-temperature alloy.
The nickel-based high-temperature alloy repairing agent comprises 50-70% of alloy powder, 25-45% of B-containing activation aid and 5% of binder in percentage by mass, and the selected binder can be completely volatilized at the temperature below 800 ℃.
The preparation method of the nickel-based high-temperature alloy repairing agent comprises the steps of uniformly mixing alloy powder and an activation auxiliary agent containing B according to a proportion, and adding a binder to prepare a paste.
The nickel-base superalloy repairing method utilizes the repairing agent and comprises the following steps:
s1: preprocessing a repair area to clean the surface of a repair position;
s2: preparing a repairing agent, and coating the repairing agent on a repairing area;
s3: placing the workpiece in a vacuum environment, and heating the workpiece to 1190-1230 ℃ at a heating speed of less than 16.8 ℃/min;
s4: keeping the temperature at 15min-40min, and cooling to room temperature along with the furnace;
s5: heating to 1200-1210 ℃ in a vacuum environment at a heating speed of less than 10 ℃/min;
s6: keeping the temperature at 100min-200min, and cooling to room temperature at a cooling rate of more than 40 ℃/min.
Further, the vacuum degree of the vacuum environment is lower than 7 x 10 -3 Pa。
Further, after step S6, the repair area is surface-sprayed.
In summary, due to the adoption of the technical scheme, the invention has the beneficial effects that:
1. after the alloy powder disclosed by the invention is matched with the B-containing activation auxiliary agent to repair the nickel-based high-temperature alloy, the high-content W, mo in the alloy powder can be greatly combined with B in the low-melting-point B-containing activation auxiliary agent to form stable and fine dispersed W boride and Mo boride, so that the loss of Cr element in a gamma phase is avoided, the generation of large boride and eutectic phase is further avoided, and the condition that the B in a repair area exists in a mode of minimizing the performance damage of the repair area is further realized.
2. After the nickel-base superalloy is repaired by the repairing agent disclosed by the invention, the content of the residual W, mo and Cr in a gamma phase of a repair area is close to that of a base material, the form, the size and the precipitation amount of a gamma' phase reach the same level as that of the repaired base material, and the repair area of the nickel-gold superalloy is ensured to have excellent oxidation resistance, thermal corrosion resistance and durability.
3. After the nickel-based high-temperature alloy is repaired by using the repairing agent disclosed by the invention, the components of main elements in gamma and gamma 'phases in a repair area are basically consistent with that of a repaired base material, the Kenkard effect is weakened during high-temperature service, the gamma and gamma' phases in the repaired base material are kept stable for a long time, and the service life of a repaired workpiece is prolonged.
Drawings
The invention will now be described, by way of example, with reference to the accompanying drawings, in which:
FIG. 1 is a micro-topography of an alloy powder of the present disclosure;
FIG. 2 shows the morphology of the IN-738LC alloy additive repair area by the repair agent disclosed IN example 3 of the present invention.
Detailed Description
All of the features disclosed in this specification, or all of the steps of any method or process so disclosed, may be combined in any combination, except combinations of features and/or steps that are mutually exclusive.
Any feature disclosed in this specification may be replaced by alternative features serving equivalent or similar purposes, unless expressly stated otherwise. That is, unless expressly stated otherwise, each feature is only an example of a generic series of equivalent or similar features.
Example 1
The nickel-based superalloy powder with the high W, mo content is characterized in that: the preparation at least comprises the following elements in percentage by mass:
c (0.05% -0.20%), cr (15.00% -20.00%), co (8.00% -12.00%), W (8.00% -12.00%), mo (10.00% -15.00%), ta (1.00% -5.00%), A l (4.00% -6.00%), T i (4.00% -6.00%), nb (0-0.60%); the balance is N i or/and unavoidable impurity elements.
The alloy powder in the embodiment has higher W, mo content, and can be matched with a low-melting-point B-containing activation auxiliary agent to repair the nickel-based high-temperature alloy as high-melting-point plastic powder; in consideration of the chemical property of the B element in the low-melting-point B-containing activation auxiliary agent, W, mo in the alloy powder can be greatly combined with the B in the low-melting-point B-containing activation auxiliary agent to form two stable borides of a W-rich boride and a Mo-rich boride which are stable and fine and dispersed, so that the loss of the Cr element in a gamma phase is avoided, further the generation of a large boride and a eutectic phase is avoided, the B in a repair area exists in a mode of minimizing the damage to the performance of the repair area, and the durability and the oxidation resistance of the repair area are effectively improved.
Specifically, C is one of the most important grain boundary strengthening elements in the nickel-base superalloy, and almost all of the nickel-base superalloy is added. The C element can be combined with one or more of Cr, ta, nb, mo, W and Ti to form beneficial carbides (wherein M represents an element or an ionic group) of the types of MC, M6C, M C3, M23C6 and the like, and the carbides are segregated to grain boundaries to prevent grain boundary sliding and crack formation, so that the improvement of the endurance time and the endurance plasticity is facilitated. However, too much carbon addition causes formation of a continuous carbide film layer on the grain boundary, makes the grain boundary brittle, and easily causes nucleation and propagation of cracks, thereby resulting in a decrease in the endurance life. Therefore, the content of C in the alloy composition of the present invention is limited to the range of 0.05wt% to 0.20 wt%.
Cr can have oxidation resistance and hot corrosion resistance, when the Cr is added too low, a continuous and compact Cr2O3 oxidation film cannot be formed on the surface of the repair area quickly, so that the oxidation resistance and the hot corrosion resistance of the repair area are lower than those of a parent metal, and if the Cr content is too high, harmful secondary phase precipitation can be promoted. Therefore, the content of Cr in the alloy composition of the present invention is limited to the range of 15.00wt% to 20.00 wt%.
Co can reduce the function of stacking layer dislocation of the matrix, so that dislocation cross slip is difficult, solid solution strengthening is caused, the Co can be infinitely mutually dissolved with a nickel-based solid solution, and the creep property of the matrix is improved in a stable state along with the increase of Co content in a certain range. Therefore, the content of Co in the alloy composition of the present invention is limited to the range of 8.00wt% to 12.00 wt%.
The addition amount of Al and Ti directly influences the precipitation amount of the gamma 'precipitation strengthening in the nickel-base superalloy, and the precipitation amount of the gamma' phase directly relates to the creep property of a repair area. In addition, ti also contributes to the strength of the alloy at high temperatures by combining with C to form MC type carbides. The contents of Al and Ti in the alloy components are limited within the range of 4.00wt% to 6.00wt%, so that the volume fraction of a gamma' phase in a repair area is ensured, and the precipitation and growth of a harmful phase eta phase are avoided as much as possible.
Both Nb and Ta added in the alloy can replace part of Al and Ti by entering the gamma 'phase, so that the composition of the gamma' phase is changed, coarsening of the gamma 'phase is inhibited, and the stability of the gamma' phase is improved, thereby improving the strength and creep resistance of a repair area. However, too much Nb and Ta addition results in the formation of a secondary phase in the repair area that is detrimental to performance, such as μ phase, laves phase, etc. Therefore, the alloy composition of the present invention is limited to a range of 0wt% to 0.60wt% for Nb and a range of 1.00wt% to 5.00wt% for Ta.
In the nickel-based superalloy, W, mo is two main strengthening elements in a gamma phase of a nickel-based solid solution, and the solid solution strengthening effect is very obvious. However, when the low-melting-point B-containing activation auxiliary agent is mixed with commercial high-melting-point powder to repair a damaged area of a workpiece, the B element is combined with the low-content W, mo in the commercial high-melting-point powder to generate boride, so that the boride loses all strengthening effects. Therefore, the content of W in the alloy composition of the invention is increased to be in the range of 8.00wt% to 12.00wt%, and the content of Mo in the alloy composition is increased to be in the range of 10.00wt% to 15.00wt%, which is far higher than the addition amount of W and Mo in the conventional nickel-base high-temperature alloy, so that the B element in the low-melting-point B-containing activation assistant is stabilized, and the rest of W and Mo which do not participate in the combination reaction with B can play a solid solution strengthening role on the gamma phase of the matrix, thereby solving the problem of poor durability of the repaired joint. Although Cr is also a generating element of boride, cr has a lower affinity for B than Mo and W, and the formed boride is unstable and easily decomposed at high temperature, and therefore Cr is not considered as a stabilizing element of boride in the design concept of the present invention. In the alloy composition of the invention, another beneficial effect of high-concentration addition of W and Mo is realized in that a great deal of Cr in a gamma phase is prevented from being greatly consumed due to combination of a great deal of Cr and B in a repair area, and the oxidation resistance and hot corrosion resistance of the repair area are ensured.
To further clarify and illustrate the technical solution of the present invention, the following non-limiting embodiments are provided, table 1 is an embodiment and a comparative example of alloy powder, and the following element content data are mass percent data.
Table 1 embodiment and comparative example (wt%) of alloy powder
It should be noted that the low melting point B-containing activating auxiliary used in the above examples and comparative examples has the same dosage and brand, i.e. the same amount of B element, except that the B element in table 1 is a compound corresponding to the diffusion form, so there is a difference in the mass percentage and the mass percentage shown when WB (n) + MoB (n) + CrB (n) is determined by the experiment, but the difference does not affect the summary of the experimental conclusion, and the specific conclusion is as follows:
in the embodiment, the alloy powder with the trade marks of DFB-70, DFB-71, DFB-72, DFB-75 and DFB-76 is matched with a low-melting-point B-containing activation auxiliary agent to carry out powder metallurgy repair on a nickel-based high-temperature component, the high-content W, mo in the powder can be greatly combined with B in the low-melting-point B-containing activation auxiliary agent, stable and fine dispersed W-rich boride and Mo-rich boride are formed in high-melting-point plastic powder, the loss of Cr element in a gamma phase is avoided, the generation of large boride and eutectic phase is avoided, after all B elements form stable boride, the content of residual W, mo and Cr in the gamma phase in a repair area is close to that of a base material, the shape, size and precipitation amount of the gamma' phase reach the same level as that of the repaired base material, and the repair joint is ensured to have excellent oxidation resistance, hot corrosion resistance and durability; in the comparative example with the mark of In738LC, mar-m247 and GTD111, when the corresponding alloy powder is matched with a low-melting-point B-containing activation auxiliary agent to carry out powder metallurgy repair on a nickel-based high-temperature component, wherein the W, mo has low content and is not enough to stabilize the B element In the low-melting-point B-containing activation auxiliary agent, so that a large amount of Cr element In high-melting-point plastic powder is consumed, a repaired tissue contains a large amount of Cr-rich boride and a low-melting-point boron-containing eutectic, the content of W, mo and Cr In a gamma phase of a repaired area is far lower than that of a base material, holes are formed after the low-melting eutectic is secondarily melted after heat treatment, a large amount of B is diffused to the side close to a welding seam of the base material and is combined with the W, mo and Cr to form boride, so that the content of the W, mo and Cr In the gamma phase of the side close to the welding seam of the base material is seriously reduced, and the tissue is seriously damaged. Therefore, the durability, high-temperature oxidation resistance and hot corrosion resistance of the repair area obtained by the alloy powder disclosed in the embodiment of the invention are all improved remarkably.
As a specific embodiment, the alloy powder has a melting temperature in the range of 1250 ℃ to 1300 ℃.
As a specific embodiment, the particle size of the alloy powder is 30 μm to 106 μm; the granularity is prepared by an atomization method; specifically, the high-temperature molten auxiliary agent is formed into powder with target granularity by adopting a high-pressure water flow, airflow atomization or ultrasonic atomization mode, so that the auxiliary agent is favorable for being more tightly piled when the alloy is repaired, and the alloy repairing performance is ensured.
When the alloy powder disclosed in this embodiment is applied to the repair of the nickel-based superalloy, the contents of Cr, co, ta, al, ti, and Nb in the alloy powder can be adjusted according to the components of the repaired substrate, and the contents of Mo and W can be adjusted according to the amount of the low-melting-point B-containing activation aid and the components of the repaired substrate; in the repairing process, B in the liquid phase is absorbed by Mo and W which are added in large quantity in the alloy powder (high-melting-point plastic powder) of the embodiment, dispersed small-size granular boride is generated in the high-melting-point plastic powder, mo, W and other elements which do not react with B in the gamma phase of the repairing area are uniformly diffused through subsequent heat treatment, so that the content of solid solution strengthening elements in the gamma phase of the repairing area is basically consistent with that of the repaired base material, the shape, size and precipitation amount of the gamma 'phase reach the same level as that of the repaired base material, the element diffusion caused by the Kirkdall effect is weakened in high-temperature service, the repaired base material and the gamma and gamma' phases of the repaired area are kept stable for a long time, and the service life of a repaired workpiece is prolonged.
Further, when the alloy powder disclosed in the embodiment is applied to nickel-based superalloy repair, the composition of the Al + Ti content in the alloy powder is adjusted, so that the form, size and precipitation amount of a gamma' phase in a repair area can reach the same level as that of a repaired base material; the component adjustment of the W + Mo content in the nickel-based high-temperature alloy powder with the high W, mo content is carried out according to the addition amount of the low-melting-point B-containing activation assistant, so that the content of W, mo and Cr in a gamma phase of a repair area can be ensured, and the durability, the high-temperature oxidation resistance and the hot corrosion resistance of the repair area are effectively improved.
IN this example, the alloy powder can be used with a low melting point B-containing activation aid to repair various high Al-Ti content Ni-based cast superalloys such as IN738LC, mar-m247, GTD-111, etc., but not limited to the above.
It should be noted that patent "CN111575536" discloses "a high W, mo content nickel-based superalloy", which reduces the aggregation degree of internal carbides and improves the uniformity of the material by changing the process manufacturing method under the premise of ensuring that the conventional mechanical properties of the material are not affected, so as to obtain the nickel-based superalloy with better comprehensive properties. The present example suggests that the alloy powder is obtained by changing the contents of the constituent elements therein to ensure the performance of the repair area.
Example 2
The nickel-based superalloy repair agent comprises the alloy powder in embodiment 1, and also comprises an activation assistant containing B and a binder, wherein the alloy powder accounts for 50-70% of the mass percent, the activation assistant containing B accounts for 25-45% of the mass percent, and the binder accounts for 5% of the mass percent.
Specifically, taking a repairing agent capable of repairing I N-738LC nickel-based superalloy as an example, alloy powder with DFB-75 mark in Table 1 in example 1 is selected, and the microscopic appearance is shown in FIG. 1. The low-melting-point B-containing activation auxiliary comprises the following elements in percentage by mass: 10.0% Cr, 10.0% Co, 3.0% Al, 2.0% Ti, 6.0% Ta, 3.0% Re, 3.0% B, the remainder N i and unavoidable impurity elements.
The preparation method of the alloy repairing agent comprises the steps of preparing the alloy repairing agent, uniformly mixing high-melting-point plastic powder and an auxiliary agent according to the mass percentages of 30% and 65% respectively, so that the same amount of the high-melting-point plastic powder and the auxiliary agent exist in a unit volume, adding a binding agent with the mass percentage of 5% to prepare a paste, enabling the repairing agent to be viscous due to the paste, reducing the fluidity, enabling the repairing agent to be stable when being coated and filled in a repairing position, and preventing the repairing agent from being separated from the repairing position before the repairing agent is heated and melted; the viscous repairing agent is more convenient to fill the repairing area, and the viscous repairing agent has certain fluidity, so that when the repairing agent is filled in the repairing position, the shape of the repairing agent can be automatically changed according to the size of the filling position due to the flowing performance of the repairing agent, the filling of the irregular repairing area is met, the repairing agent can be completely filled under the action of the fluidity of the repairing agent, and the defect gap existing in the repairing area is reduced.
Example 3
In this example, the method of repairing I N-738LC nickel-base superalloy with the repair agent described in example 2 includes the steps of:
s1: preprocessing a repair area to clean the surface of a repair position;
s2: preparing a repairing agent, and coating the repairing agent on a repairing area;
s3: placing the workpiece in a vacuum environment, and heating the workpiece to 1190-1230 ℃ at a heating speed of less than 16.8 ℃/min;
s4: keeping the temperature at 15min-40min, and cooling to room temperature along with the furnace;
s5: heating to 1200-1210 ℃ in a vacuum environment at a heating speed of less than 10 ℃/min;
s6: after ensuring that 100min-200min, cooling to room temperature at a cooling speed of more than 40 ℃/min.
Specifically, the method comprises the steps of repairing defects (repair areas) of I N-738LC nickel-based superalloy, wherein the length, the width and the height of each defect are 40mm, 3mm and 2mm respectively, and in the step S1, the defects in the repair areas are polished completely to avoid the influence of impurities on defect repair; in step S2, the process and method for preparing the repair agent are described in detail in example 2, and the repair area is coated with the repair agent to complete the additive addition of the repair area; then, putting the workpiece into a vacuum heat treatment furnace for material increase connection treatment, wherein the heating speed is 10 ℃/min, the sintering temperature is 1190 ℃, the temperature is kept for 30min, the vacuum degree is superior to 7 x 10 < -3 > Pa, and the workpiece is cooled to room temperature along with the furnace after the temperature is kept; after the material adding connection of the workpiece is finished, heating the workpiece in a vacuum furnace to 1200 ℃ at a heating speed of less than 10 ℃/min, preserving heat for 120min, and then cooling the workpiece to room temperature at a cooling speed of more than 40 ℃/min.
Furthermore, the heating in the vacuum environment can effectively control the N element in the gas of the material, reduce the content of the N element in the gas in the material from 300ppm on average to less than or equal to 50ppm, and ensure that the vacuum degree in the vacuum environment is lower than 7 multiplied by 10 -3 Pa。
It should be noted that, for the heating speed, the heating speed is limited by the heating boiler, and in order to ensure the uniform heating of the workpiece, the heating speed needs to be controlled below 16.8 ℃/min; selecting the heat preservation time, preserving heat for enough time, and completely filling the restoration area with the restoration agent and uniformly expanding the restoration area; as for the cooling speed, the rapid cooling at 40 ℃/min can ensure that the repairing area forms a gamma' phase with excellent form, and the tensile property, the durability and the creep property of the repairing area are ensured.
After step S6, the repaired area is surface sprayed to further improve the oxidation resistance of the repaired area.
IN this embodiment, the performance test of the IN-738LC Ni-based superalloy after repairing the defects with the length, width and height of 40mm, 3mm and 2mm respectively is as follows:
as shown IN FIG. 2, the repairing agent is applied to the tissue morphology of the IN-738LC nickel-based alloy additive repairing area.
The composition of the repaired area and the gamma + gamma' phase within the substrate grains were determined as shown in table 2.
TABLE 2 average composition comparison (wt%) of the repair area to the gamma + gamma' phase inside the substrate grains
| Region(s) | Cr | Co | W | Mo | Ti | Al | Ta | Nb | Ni |
| Repair area | 18.2 | 10.1 | 1.2 | 3.2 | 4.0 | 4.4 | 1.6 | 0.2 | Bal. |
| Base material | 15.8 | 8.2 | 2.7 | 1.7 | 3.2 | 3.3 | 1.7 | 0.7 | Bal. |
As can be seen from Table 2, the chemical compositions of the two regions to be measured are close.
Tensile properties of the repaired joints were measured and the results are shown in table 3.
TABLE 3 tensile Properties of the repaired joints
The durability of the repaired joints was measured and the results are shown in table 4.
TABLE 4 endurance performance of repaired joints
The invention is not limited to the foregoing embodiments. The invention extends to any novel feature or any novel combination of features disclosed in this specification and any novel method or process steps or any novel combination of features disclosed.
Claims (10)
1. The nickel-based superalloy powder with the high W, mo content is characterized in that: the preparation at least comprises the following elements in percentage by mass:
c (0.05% -0.20%), cr (15.00% -20.00%), co (8.00% -12.00%), W (8.00% -12.00%), mo (10.00% -15.00%), ta (1.00% -5.00%), al (4.00% -6.00%), ti (4.00% -6.00%), nb (0-0.60%); the rest is Ni or/and inevitable impurity elements.
2. The high W, mo content nickel-base superalloy powder of claim 1, wherein: the content of Cr, co, ta, al, ti and Nb in the alloy powder can be adjusted according to the components of the repaired base material; the contents of Mo and W can be adjusted according to the amount of the low-melting-point B-containing activation aid and the components of the repair base material.
3. The high W, mo content nickel-base superalloy powder of claim 1, wherein: the melting temperature of the alloy powder ranges from 1250 ℃ to 1300 ℃.
4. The high W, mo content nickel-base superalloy powder of claim 1, wherein: the particle size of the alloy powder is 30-106 μm.
5. Use of the alloy powder according to any one of claims 1 to 4 for nickel-base superalloy repair.
6. A nickel-base superalloy repair agent comprising the alloy powder of any of claims 1 to 4, wherein: the alloy powder comprises 50-70% of B-containing activation assistant and 25-45% of binder by mass percentage.
7. A method for preparing a nickel-base superalloy repair agent, the repair agent of claim 6 being prepared by: the alloy powder and the activating assistant containing B are mixed in certain proportion and mixed with adhesive to form paste.
8. The method for repairing a nickel-base superalloy by using the repairing agent according to claim 6, wherein the repairing agent comprises the following components: the method comprises the following steps:
s1: preprocessing a repair area to clean the surface of a repair position;
s2: preparing a repairing agent, and coating the repairing agent on a repairing area;
s3: placing the workpiece in a vacuum environment, and heating the workpiece to 1190-1230 ℃ at a heating speed of less than 16.8 ℃/min;
s4: keeping the temperature for 15-40 min, and cooling to room temperature along with the furnace;
s5: heating to 1200-1210 ℃ in a vacuum environment at a heating speed of less than 10 ℃/min;
s6: keeping the temperature for 100-200 min, and cooling to room temperature at a cooling rate of more than 40 ℃/min.
9. The nickel-base superalloy repair method of claim 8, wherein: the vacuum degree of the vacuum environment is lower than 7 x 10 -3 Pa。
10. The nickel-base superalloy repair method of claim 8, wherein: after step S6, the repair area is surface-sprayed.
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