CN112388143A - Method for welding nickel-based single crystal superalloy TLP (thermal shock welding) of mixed powder interlayer - Google Patents
Method for welding nickel-based single crystal superalloy TLP (thermal shock welding) of mixed powder interlayer Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/002—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating specially adapted for particular articles or work
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/24—Preliminary treatment
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Abstract
A TLP welding method for nickel-based single crystal superalloy with a mixed powder intermediate layer relates to a TLP welding method for nickel-based alloy. The purpose is to solve the problem that the performance of a joint is reduced due to the fact that a welding line generates a brittle phase in the welding process of the nickel-based single crystal superalloy. The method comprises the following steps: polishing and cleaning the nickel-based single crystal superalloy, smearing BNi2 powder and Al powder mixed brazing filler metal on the surface to be welded, and performing TLP diffusion welding. The method introduces the mixed powder intermediate layer in the liquid phase diffusion bonding process, reduces the brittle phase by adding the Al element, and improves the reliability of the welding line. The invention is suitable for the TLP welding of the nickel-based single crystal superalloy.
Description
Technical Field
The invention relates to a TLP welding method for a nickel-based alloy.
Background
Aeroengine turbine blades are subjected to complex stress environments and severe temperature loads, so the requirements on materials are extremely strict. Therefore, in order to meet the working requirements of the turbine blade of the engine, on one hand, the structure of the blade is optimally designed, so that the aim of rapid cooling is fulfilled; another aspect is to make and use more temperature resistant alloy materials. Compared with iron-based and cobalt-based alloys, the nickel-based alloy has the advantages of superior performance, stable structure, strong oxidation resistance and corrosion resistance, and can work in high-temperature and complex stress environments.
Ni3Al is single crystal superalloy, has the characteristics of higher strength, good creep and fatigue resistance, excellent oxidation resistance and hot corrosion resistance, reliable structure and the like, and has R phenomenon (at 0.4T)m<T<0.7TmIn the range, the higher the temperature is, the higher the strength is), the grain boundary which is a high-temperature weak link is eliminated, and the material is a reliable material which can be applied to aeroengine turbine blades. However, since the preparation process of the single crystal blade is complex and the manufacturing cost is expensive, the blade is scrapped due to the problems of cracks, oxidation and the like during service. The repair connection is carried out on the parts, so that the cost and the resource can be saved, and the service life of the parts can be prolonged to a certain extent.
The nickel-based single crystal superalloy is a main material of the prior advanced engine turbine blade, and reliable high-temperature performance is realized by solid solution strengthening of a gamma 'phase and precipitation strengthening of the gamma' phase and the gamma phase due to the fact that a base material contains elements such as chromium, tungsten and molybdenum. When the (Al + Ti) content in the base material exceeds 6 wt.% during welding, a brittle phase such as eutectic structure, carbide, boride, etc. is easily generated in the weld, and foreign crystals are induced to affect cracks in the heat affected zone, and the occurrence of these defects deteriorates the uniformity of the single crystal structure, resulting in a decrease in the overall properties of the material.
Transient liquid phase diffusion welding (TLP welding) has the advantages of brazing and diffusion welding, can be flexibly applied to connection of novel materials, and as the heat preservation time is prolonged, as the melting-down element diffuses to the base material, the welding seam is changed from a liquid phase to a solid phase again, and then the organization and the components are homogenized, and finally reliable connection with high performance is realized. Therefore, the advanced welding technology of the nickel-based single crystal superalloy is researched, the reliable connection and repair of the nickel-based single crystal superalloy are realized, and the method has important significance for the production and the manufacture of aero-engines and the promotion of the development of the aviation industry in China.
Disclosure of Invention
The invention provides a TLP diffusion welding method for nickel-based single crystal superalloy with a mixed powder interlayer, aiming at solving the problem that the performance of a joint is reduced due to the fact that a weld joint generates a brittle phase in the welding process of the nickel-based single crystal superalloy.
The method for performing TLP diffusion welding on the nickel-based single crystal superalloy in the mixed powder intermediate layer comprises the following steps:
step-by-step polishing the surface to be welded of the nickel-based single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, mixing BNi2 powder and Al powder, adding ethylene glycol, uniformly mixing to obtain a paste solder, uniformly coating the paste solder on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys with a graphite block to ensure that the layers are in close contact with each other to obtain a part to be welded;
and thirdly, performing TLP diffusion bonding on the to-be-welded piece obtained in the step two, and thus finishing.
The principle and the beneficial effects of the invention are as follows:
the method introduces the mixed powder intermediate layer in the liquid phase diffusion connection process, generates a gamma' phase through the reaction of the Al element and the Ni element, changes the distribution of the original continuous eutectic structure and precipitated phases, shunts the low-melting-point liquid phase between phase boundaries, enables the low-melting-point liquid phase to be dissociated in the welding line, and realizes isothermal solidification of the welding line along with the temperature rise. Meanwhile, reaction products in the welding seam are dissolved and diffused to a certain degree along with the increase of the heat preservation time, the volume of a eutectic structure region and brittle phases such as CrB and the like in the joint is greatly reduced or even disappears, the black CrB phase tends to be distributed in a dispersed manner, the reliability of the welding seam is improved, and the average shear strength of the obtained brazed joint can reach 550 MPa.
Drawings
FIG. 1 is a microstructure of a connection joint obtained in example 1;
FIG. 2 is a low magnification view of FIG. 1;
FIG. 3 is a magnified view of the area c in FIG. 1;
FIG. 4 is a magnified view of the area d in FIG. 2;
FIG. 5 is a microstructure of the connection joint obtained in comparative experiment 1;
FIG. 6 is a microstructure map of the diffusion zone and weld joint interface of the connection joint obtained in comparative experiment 1.
Detailed Description
The technical scheme of the invention is not limited to the specific embodiments listed below, and any reasonable combination of the specific embodiments is included.
The first embodiment is as follows: the method for performing TLP diffusion welding on the nickel-based single crystal superalloy in the mixed powder intermediate layer comprises the following steps:
step-by-step polishing the surface to be welded of the nickel-based single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, mixing BNi2 powder and Al powder, adding ethylene glycol, uniformly mixing to obtain a paste solder, uniformly coating the paste solder on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys with a graphite block to ensure that the layers are in close contact with each other to obtain a part to be welded;
and thirdly, performing TLP diffusion bonding on the to-be-welded piece obtained in the step two, and thus finishing.
According to the method, the mixed powder intermediate layer is introduced in the liquid phase diffusion connection process, the gamma' phase is generated through the reaction of the Al element and the Ni element, the distribution of the original continuous eutectic structure and precipitated phases is changed, the low-melting-point liquid phase is shunted between phase boundaries and dissociated in the welding line, and the isothermal solidification of the welding line is realized along with the temperature rise. Meanwhile, reaction products in the welding seam are dissolved and diffused to a certain degree along with the increase of the heat preservation time, the volume of a eutectic structure region and brittle phases such as CrB and the like in the joint is greatly reduced or even disappears, the black CrB phase tends to be distributed in a dispersed manner, the reliability of the welding seam is improved, and the average shear strength of the obtained brazed joint can reach 550 MPa.
The second embodiment is as follows: the first difference between the present embodiment and the specific embodiment is: and in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded.
The third concrete implementation mode: the present embodiment differs from the first or second embodiment in that: in the first step, the ultrasonic cleaning time is 5-10 min.
The fourth concrete implementation mode: the difference between this embodiment mode and one of the first to third embodiment modes is: and in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1 (5-10).
The fifth concrete implementation mode: the difference between this embodiment and one of the first to fourth embodiments is: in the second step, the mass ratio of the BNi2 powder to the Al powder is (91-97): 3-9.
The sixth specific implementation mode: the difference between this embodiment and one of the first to fifth embodiments is: and in the second step, mixing BNi2 powder and Al powder in a ball mill, wherein the ball mill is used for ball milling in Ar gas atmosphere, the rotating speed of the ball mill is 200r/min, the mixing time is 15-20 min, and the ball-to-material ratio is 0.4-0.6.
The seventh embodiment: the difference between this embodiment and one of the first to sixth embodiments is: in the second step, the paste-shaped brazing filler metal is coated to the thickness of 90-110 mu m. And step two, when the paste-shaped brazing filler metal is coated, foils with certain thicknesses are used as spacers to be attached to two sides of the surface to be coated, the paste-shaped brazing filler metal is coated between the foils, the coating thickness of the paste-shaped brazing filler metal is limited by the thickness of the foils, and then the paste-shaped brazing filler metal is scraped to ensure that the coated brazing filler metal is uniform in thickness.
The specific implementation mode is eight: the present embodiment differs from one of the first to seventh embodiments in that: the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly, vacuum-pumping is carried out to 2 x 10-2Pa, then heating to 1040-1140 ℃, preserving heat for 0.5-3 h, and cooling to room temperature along with the furnace to complete the process.
The specific implementation method nine: the present embodiment differs from the first to eighth embodiments in that: in the second step, the particle size of the BNi2 powder is 38-75 μm.
The detailed implementation mode is ten: the present embodiment differs from one of the first to ninth embodiments in that: and in the second step, the grain diameter of the Al powder is 38-48 mu m.
Example 1:
the TLP diffusion welding method for the nickel-based single crystal superalloy with the mixed powder intermediate layer in this example was performed according to the following steps:
step-by-step polishing the surface to be welded of the IC10 single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
the surface to be welded in the step one is vertical to the solidification direction of the single crystal superalloy of IC10, and a welding seam obtained after welding is vertical to the directional solidification direction;
in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded;
in the first step, the ultrasonic cleaning time is 5 min;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, mixing BNi2 powder and Al powder, adding ethylene glycol, uniformly mixing to obtain a paste solder, uniformly coating the paste solder on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys with a graphite block to ensure that the layers are in close contact with each other to obtain a part to be welded;
in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1: 6;
in the second step, the mass ratio of the BNi2 powder to the Al powder is 97: 3;
mixing BNi2 powder and Al powder in the second step in a ball mill, wherein the ball mill is in Ar gas atmosphere, the rotating speed of the ball mill is 200r/min, the mixing time is 17min, and the ball-to-material ratio is 0.5;
in the second step, the particle size of the BNi2 powder is 38-75 μm;
in the second step, the grain size of the Al powder is 38-48 mu m;
in the second step, the paste-shaped brazing filler metal is coated to the thickness of 100 mu m;
thirdly, performing TLP diffusion welding on the to-be-welded piece obtained in the second step to finish the operation;
the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly vacuum pumping is carried outEmpty to 2X 10-2Pa, then heating to 1100 ℃, keeping the temperature for 2 hours, and cooling to room temperature along with the furnace to complete the process.
Comparative experiment 1:
the experimental nickel-based single crystal superalloy TLP diffusion welding method is carried out according to the following steps:
step-by-step polishing the surface to be welded of the IC10 single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
the surface to be welded in the step one is vertical to the solidification direction of the single crystal superalloy of IC10, and a welding seam obtained after welding is vertical to the directional solidification direction;
in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded;
in the first step, the ultrasonic cleaning time is 5 min;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, uniformly mixing BNi2 powder and ethylene glycol to obtain a paste brazing filler metal, uniformly coating the paste brazing filler metal on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys by using a graphite block to ensure that the layers are in close contact with each other to obtain a piece to be welded;
in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1: 6;
in the second step, the particle size of the BNi2 powder is 38-75 μm;
in the second step, the paste-shaped brazing filler metal is coated to the thickness of 100 mu m;
thirdly, performing TLP diffusion welding on the to-be-welded piece obtained in the second step to finish the operation;
the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly, vacuum-pumping is carried out to 2 x 10-2Pa, then heating to 1100 ℃, keeping the temperature for 2 hours, and cooling to room temperature along with the furnace to complete the process.
FIG. 1 is a microstructure of a connection joint obtained in example 1; FIG. 2 is a low magnification view of FIG. 1; FIG. 3 is a magnified view of the area c in FIG. 1; FIG. 4 is a magnified view of the area d in FIG. 2; in FIGS. 1-4, ISZ is an isothermal solidification zone, NSZ is a non-isothermal solidification zone, DAZ is a diffusion zone, and BMZ is a base metal zone; Cr-W-Si compounds are at P1, boride eutectic structures are at P2 and P5, a gamma phase is at P3, and a bulk Cr-W-Si phase is at P4; p6 is granular precipitated phase in the diffusion region, P7 is needle-shaped precipitated phase in the diffusion region;
FIG. 5 is a microstructure of the connection joint obtained in comparative experiment 1; FIG. 6 is a microstructure of the interface between the diffusion region and the weld of the joint obtained in comparative experiment 1; in FIGS. 5 and 6, ISZ is the isothermal solidification zone, NSZ is the non-isothermal solidification zone, DAZ is the diffusion zone, and BMZ is the base metal zone; Cr-W-Si compound at P1, eutectic structure of B compound at P2, gamma phase at P3,
the comparison of the figures 1-6 shows that the distribution of weld joint tissues and phases is effectively regulated and controlled by adding the Al element, the joint is not characterized in that a continuously distributed eutectic tissue and a precipitated phase exist in the center of the weld joint, but a low-melting-point liquid phase is shunted between phase boundaries, and reaction products in the weld joint are dissolved and diffused to a certain extent, so that the joint performance is effectively improved.
An electronic universal tester is used for carrying out a shearing test, the loading speed is 0.5mm/min, and the average room temperature shearing strength of the connecting joint obtained in the example 1 by adopting a BNi2+ Al mixed powder intermediate layer IC10 single crystal high temperature alloy TLP diffusion welding method reaches 550 MPa. Under the same parameters, the room temperature shear strength of the connector joint obtained by direct TLP diffusion welding of the BNi2 intermediate layer in the comparative test 1 is only 473 MPa.
Example 2:
the TLP diffusion welding method for the nickel-based single crystal superalloy with the mixed powder intermediate layer in this example was performed according to the following steps:
step-by-step polishing the surface to be welded of the IC10 single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
the surface to be welded in the step one is vertical to the solidification direction of the single crystal superalloy of IC10, and a welding seam obtained after welding is vertical to the directional solidification direction;
in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded;
in the first step, the ultrasonic cleaning time is 5 min;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, mixing BNi2 powder and Al powder, adding ethylene glycol, uniformly mixing to obtain a paste solder, uniformly coating the paste solder on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys with a graphite block to ensure that the layers are in close contact with each other to obtain a part to be welded;
in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1: 6;
in the second step, the mass ratio of the BNi2 powder to the Al powder is 97: 3;
mixing BNi2 powder and Al powder in the second step in a ball mill, wherein the ball mill is in Ar gas atmosphere, the rotating speed of the ball mill is 200r/min, the mixing time is 17min, and the ball-to-material ratio is 0.5;
in the second step, the particle size of the BNi2 powder is 38-75 μm;
in the second step, the grain size of the Al powder is 38-48 mu m;
in the second step, the paste-shaped brazing filler metal is coated to the thickness of 100 mu m;
thirdly, performing TLP diffusion welding on the to-be-welded piece obtained in the second step to finish the operation;
the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly, vacuum-pumping is carried out to 2 x 10-2Pa, then raising the temperature to 1120 ℃, preserving the heat for 2 hours, and cooling to room temperature along with the furnace to complete the process.
Comparative experiment 2:
the experimental nickel-based single crystal superalloy TLP diffusion welding method is carried out according to the following steps:
step-by-step polishing the surface to be welded of the IC10 single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
the surface to be welded in the step one is vertical to the solidification direction of the single crystal superalloy of IC10, and a welding seam obtained after welding is vertical to the directional solidification direction;
in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded;
in the first step, the ultrasonic cleaning time is 5 min;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, uniformly mixing BNi2 powder and ethylene glycol to obtain a paste brazing filler metal, uniformly coating the paste brazing filler metal on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys by using a graphite block to ensure that the layers are in close contact with each other to obtain a piece to be welded;
in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1: 6;
in the second step, the particle size of the BNi2 powder is 38-75 μm;
in the second step, the paste-shaped brazing filler metal is coated to the thickness of 100 mu m;
thirdly, performing TLP diffusion welding on the to-be-welded piece obtained in the second step to finish the operation;
the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly, vacuum-pumping is carried out to 2 x 10-2Pa, then raising the temperature to 1120 ℃, preserving the heat for 2 hours, and cooling to room temperature along with the furnace to complete the process.
An electronic universal tester is used for carrying out a high-temperature tensile test at 1000 ℃, the loading speed is 0.5mm/min, and the tensile strength of the connecting joint obtained in the embodiment 2 by adopting a BNi2+ Al mixed powder intermediate layer nickel-based single crystal superalloy TLP diffusion welding method at 1000 ℃ reaches 108 MPa. Under the same parameters, the tensile strength of the connecting joint obtained by introducing BNi2 intermediate layer direct TLP diffusion welding in comparative test 2 is only 60MPa at the high temperature of 1000 ℃.
Example 3:
the TLP diffusion welding method for the nickel-based single crystal superalloy with the mixed powder intermediate layer in this example was performed according to the following steps:
step-by-step polishing the surface to be welded of the IC10 single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
the surface to be welded in the step one is vertical to the solidification direction of the single crystal superalloy of IC10, and a welding seam obtained after welding is vertical to the directional solidification direction;
in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded;
in the first step, the ultrasonic cleaning time is 5 min;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, mixing BNi2 powder and Al powder, adding ethylene glycol, uniformly mixing to obtain a paste solder, uniformly coating the paste solder on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys with a graphite block to ensure that the layers are in close contact with each other to obtain a part to be welded;
in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1: 6;
in the second step, the mass ratio of the BNi2 powder to the Al powder is 97: 3;
mixing BNi2 powder and Al powder in the second step in a ball mill, wherein the ball mill is in Ar gas atmosphere, the rotating speed of the ball mill is 200r/min, the mixing time is 17min, and the ball-to-material ratio is 0.5;
in the second step, the particle size of the BNi2 powder is 38-75 μm;
in the second step, the grain size of the Al powder is 38-48 mu m;
in the second step, the paste-shaped brazing filler metal is coated to the thickness of 100 mu m;
thirdly, performing TLP diffusion welding on the to-be-welded piece obtained in the second step to finish the operation;
the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly, vacuum-pumping is carried out to 2 x 10-2Pa, then heating to 1100 ℃, keeping the temperature for 3 hours, and cooling to room temperature along with the furnace to complete the process.
An electronic universal tester is used for carrying out a shearing test, the loading speed is 0.5mm/min, and the room-temperature shearing strength of the connecting joint obtained in the embodiment 3 by adopting a BNi2+ Al mixed powder intermediate layer nickel-based single crystal superalloy TLP diffusion welding method reaches 537 MPa.
Claims (10)
1. A method for performing TLP (thermal liquid phase) diffusion welding on a nickel-based single crystal superalloy with a mixed powder intermediate layer is characterized by comprising the following steps of: the method comprises the following steps:
step-by-step polishing the surface to be welded of the nickel-based single crystal superalloy, and then putting the polished surface into absolute ethyl alcohol for ultrasonic cleaning to obtain the nickel-based single crystal superalloy to be welded;
secondly, taking two nickel-based single crystal high-temperature alloys to be welded, mixing BNi2 powder and Al powder, adding ethylene glycol, uniformly mixing to obtain a paste solder, uniformly coating the paste solder on the surface to be welded of one of the nickel-based single crystal high-temperature alloys to be welded, oppositely stacking the surfaces to be welded of the two nickel-based single crystal high-temperature alloys to be welded, and then pressing the two nickel-based single crystal high-temperature alloys with a graphite block to ensure that the layers are in close contact with each other to obtain a part to be welded;
and thirdly, performing TLP diffusion bonding on the to-be-welded piece obtained in the step two, and thus finishing.
2. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: and in the first step, 80# to 400# metallographic abrasive paper is adopted to polish the surface to be welded.
3. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: in the first step, the ultrasonic cleaning time is 5-10 min.
4. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: and in the second step, the mass ratio of the BNi2 powder to the ethylene glycol is 1 (5-10).
5. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: in the second step, the mass ratio of the BNi2 powder to the Al powder is (91-97): 3-9.
6. The method of claim 1, wherein: and in the second step, mixing BNi2 powder and Al powder in a ball mill, wherein the ball mill is used for ball milling in Ar gas atmosphere, the rotating speed of the ball mill is 200r/min, the mixing time is 15-20 min, and the ball-to-material ratio is 0.4-0.6.
7. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: in the second step, the paste-shaped brazing filler metal is coated to the thickness of 90-110 mu m.
8. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: the TLP diffusion bonding process in the second step comprises the following steps: in a vacuum annealing furnace, firstly, vacuum-pumping is carried out to 2 x 10-2Pa, then heating to 1040-1140 ℃, preserving heat for 0.5-3 h, and cooling to room temperature along with the furnace to complete the process.
9. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: in the second step, the particle size of the BNi2 powder is 38-75 μm.
10. The TLP diffusion welding method for nickel-based single crystal superalloys of mixed powder interlayers of claim 1, characterized in that: and in the second step, the grain diameter of the Al powder is 38-48 mu m.
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| Publication number | Priority date | Publication date | Assignee | Title |
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