CN114654070B - Connection method of dissimilar gamma' -phase reinforced superalloy - Google Patents

Connection method of dissimilar gamma' -phase reinforced superalloy Download PDF

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CN114654070B
CN114654070B CN202210297581.4A CN202210297581A CN114654070B CN 114654070 B CN114654070 B CN 114654070B CN 202210297581 A CN202210297581 A CN 202210297581A CN 114654070 B CN114654070 B CN 114654070B
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alloy
furnace
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CN114654070A (en
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夏兴川
冯浩敏
丁俭
杨轶凯
王玉江
刘永长
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Hebei University of Technology
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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
    • B23K20/02—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by means of a press ; Diffusion bonding
    • B23K20/023—Thermo-compression bonding
    • B23K20/026—Thermo-compression bonding with diffusion of soldering material
    • 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
    • B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
    • 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
    • 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
    • B23K20/26—Auxiliary equipment
    • 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
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/18—Dissimilar materials
    • 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
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/30—Nuclear fission reactors

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  • Mechanical Engineering (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)

Abstract

The invention relates to a method for connecting dissimilar gamma' -phase reinforced superalloy. The method realizes fine regulation and control of the pre-weld structure of the base metal through the processes of stress annealing, solid solution, aging treatment and the like, adjusts the TLP diffusion connection process and the inter-diffusion behavior between the interlayer alloy and the base metal according to the pre-weld structure, and solves 718Plus alloy and Ni 3 The problems of rapid precipitation of gamma' phase and large microstructure change of Al-based alloy in the TLP diffusion connection process are avoided, defects such as cavities, cracks and coarse hard alloy in a joint area are avoided, and the TLP diffusion connection joint with uniform microstructure and good mechanical property is obtained.

Description

Connection method of dissimilar gamma' -phase reinforced superalloy
Technical Field
The invention belongs to the technical field of high-temperature alloy welding, and particularly relates to a transient liquid phase diffusion connection method for realizing heterogeneous gamma' -phase reinforced high-temperature alloy.
Background
ATI718Plus (718 Plus for short) is a deformed nickel-based superalloy, which has excellent high-temperature strength, high-temperature creep property, tissue stability and hot workability, and is an ideal material for preparing turbine discs of aeroengines. Ni (Ni) 3 The Al-based alloy is a high-temperature alloy capable of being used for a long time at 850-1100 ℃, has the characteristics of low density, high specific strength, specific stiffness, high melting point and the like, has good oxidation resistance and creep resistance in a larger temperature range, and is mainly applied to heat-resistant parts of aeroengines. Realize 718Plus alloy and Ni 3 The reliable connection between Al-based alloys can fully exert the advantages of the two alloys, forThe development of the high-temperature-resistant integral structural member has important practical significance. Previous studies have shown that when using a fusion welded connection 718Plus alloy, the joint region produces a strong redistribution of solute elements, which readily forms Laves phases, TCP phases, MC-type carbides, carbonitrides, etc., thereby inducing thermal cracking and strain-age cracking. Ni (Ni) 3 Because of higher (Al+Ti) element content, the gamma' -phase of the main strengthening phase is higher in precipitation speed, so that the alloy is higher in thermal cracking sensitivity and serious in welding cracking tendency, and the alloy cannot be connected or repaired by conventional fusion welding, so that the application of the alloy to welded integral structural members is limited.
The Transient Liquid Phase (TLP) diffusion connection is a process method for forming reliable connection through mutual diffusion between the alloy of an intermediate layer and atoms of a base metal under the conditions of high vacuum degree and high temperature, combines the advantages of simple high-temperature brazing process and high solid diffusion connection strength, and is expected to realize 718Plus and Ni 3 High-efficiency connection of Al-based alloy. CN 113732479A and US 11837489 disclose the realization of a G115 heat resistant steel/Inconel 740 superalloy and Al using a TLP welding process 2 O 3 The ceramic material is effectively connected, so that the problems of low strength, poor stability and the like of the welding joint are solved. CN 113403559A and EP 3 589 760 B1 respectively disclose TLP connection processes of an Inconel 718/Rene'41 alloy and a Haynes 282/Inconel 718 alloy, and improve the performance of a base material through heat treatment, and simultaneously enable a welding seam to meet corresponding mechanical performance requirements. It can be seen that TLP diffusion bonding can achieve reliable bonding between dissimilar materials, but TLP diffusion bonding methods for dissimilar gamma prime phase strengthened superalloys are reported to be less. This is mainly because in the conventional fusion welding process, the gamma' -phase precipitation speed is high, and the microstructure of the alloy is greatly changed, which is unfavorable for obtaining a welding joint with good performance.
Disclosure of Invention
The invention aims at fusion welding the dissimilar gamma prime phase alloy (718 Plus and Ni 3 Al-based alloy) provides a method for connecting dissimilar gamma' -phase reinforced superalloy. The method realizes fine regulation and control of the pre-weld structure of the base material by optimizing the heat treatment process, and adjusts the TLP diffusion joint worker according to the pre-weld structureThe mutual diffusion behavior between the process and intermediate layer alloy and the parent metal solves the problems of 718Plus alloy and Ni 3 The problems of rapid precipitation of gamma' phase and large microstructure change of Al-based alloy in the TLP diffusion connection process are avoided, defects such as cavities, cracks and coarse hard alloy in a joint area are avoided, and the TLP diffusion connection joint with uniform microstructure and good mechanical property is obtained.
The technical scheme of the invention is as follows:
a method for joining dissimilar gamma prime phase strengthened superalloys, the method comprising the steps of:
step one, pretreatment: ni is added with 3 Processing Al-based alloy and 718Plus alloy to the required size;
step two, stress relief annealing is carried out to Ni 3 The Al-based alloy ingot is kept at 750-950 ℃ for 1-5 hours, and the furnace is cooled to room temperature after the heat preservation is finished; preserving the heat of the forged 718Plus blank at 600-900 ℃ for 1-8 hours, and cooling the blank to room temperature after the heat preservation is finished;
step three, solution treatment: ni obtained in the second step 3 The Al-based alloy is insulated for 4 to 10 hours at 1180 to 1290 ℃, and is cooled to room temperature after the insulation is finished; preserving the temperature of 718Plus alloy obtained in the second step at 950-1150 ℃ for 3-8 hours, and cooling to room temperature after the heat preservation is finished;
the cooling mode is furnace cooling, water cooling or air cooling.
Step four, aging treatment: ni obtained in the third step 3 The Al-based alloy is insulated for 6 to 10 hours at 900 to 1000 ℃, then is insulated for 4 to 6 hours at 1050 to 1150 ℃, and is cooled to room temperature after the insulation is finished; the 718Plus alloy in the third step is insulated for 6 to 10 hours at the temperature of 700 to 720 ℃, then is insulated for 5 to 8 hours at the temperature of 720 to 750 ℃, and is cooled to room temperature after the insulation is finished;
step five, surface treatment: ni obtained in the fourth step 3 Grinding and polishing the to-be-welded parts of the Al-based alloy and the 718Plus alloy, ultrasonically cleaning the to-be-welded parts in acetone for 10 to 30 minutes, flushing the to-be-welded surfaces with alcohol, and drying with cold air for later use;
the polishing is to sequentially process the surface of the base material by using 400# abrasive paper, 600# abrasive paper, 800# abrasive paper, 1000# abrasive paper, 1500# abrasive paper and 2000# abrasive paper, and the polishing is to carry out finishing processing on the surface of the base material by using diamond polishing paste.
Step six, preparing a TLP diffusion connection structure: the foil strip of the interlayer material and the two alloys obtained in the fifth step are respectively 718Plus alloy/interlayer/Ni according to the upper, middle and lower parts 3 Stacking Al-based alloys to obtain a TLP structure to be connected;
step seven, implementing TLP diffusion connection: placing the TLP structure to be connected obtained in the sixth step in a vacuum diffusion furnace, applying an axial pressure of 0.1-0.5 MPa, closing a furnace door, and vacuumizing to a vacuum degree of 10 -2 ～10 -3 Pa; then heating the vacuum diffusion furnace to 1000-1150 ℃, preserving heat for 5-120 minutes after reaching the temperature, or applying connection pressure to the TLP connection structure in the diffusion furnace for preserving heat for 5-120 minutes, and cooling to room temperature along with the furnace after the heat preservation is finished, thus obtaining the required sample.
The connection pressure applied in the step seven is 0.2-3.0 MPa.
The interlayer material is interlayer alloys such as BNi-2, BNi-3, BNi-9 or Mn-Ni-Cr.
The alloy in the second to fourth steps is placed in a high temperature resistant corundum crucible, the corundum crucible is required to be preheated before being used, the preheating temperature is 400-600 ℃, and the preheating time is 2-6 hours to ensure that the crucible is sufficiently dried. The heat preservation process is carried out in a box-type resistance furnace, and the box-type resistance furnace has the functions of rapid temperature rise and fall, temperature rise and fall rate control and the like.
In the seventh step, the temperature rising process of reaching the heat preservation temperature is as follows: the temperature rising rate from room temperature to 500 ℃ is 5-7 ℃/min, and the furnace temperature is kept for 20-30 minutes after reaching 500 ℃; the temperature rising rate in the process of 500 ℃ to 900 ℃ is 3 to 4 ℃/min, and when the furnace temperature reaches 900 ℃, the temperature is kept for 15 to 30 minutes; the temperature rising rate from 900 ℃ to the target temperature is controlled to be 2-3 ℃/min, and the target temperature is reached.
The invention has the substantial characteristics that:
in the prior art, in the aspect of the connection of dissimilar gamma ' -phase alloys, the connection research of the gamma ' -phase alloys is less due to the problem of rapid precipitation of gamma ' -phase; secondly, in the existing pre-welding heat treatment method, solid solution, aging or solid solution and aging treatment is mostly adopted, and the stress relief annealing is firstly carried out, and then the solid solution, aging or solid solution and aging heat treatment process is less; finally, the base metal alloy has larger structure change in the heat treatment process, and stable structure can be obtained by not performing a certain heat treatment process like the common alloy.
The invention uses the heat treatment process (different heat treatment process collocation, heat preservation temperature, heat preservation time, cooling and other modes) before welding to carry out the grain size, gamma' phase, eta phase and carbide content, distribution and Ni of 718Plus alloy 3 The conditions of the microstructure of the Al-based alloy dual-phase region (gamma+gamma '), eutectic region (gamma-gamma'), (gamma+gamma ')/(gamma-gamma') interface region, the content, distribution, size, type and the like of gamma '-phase and MC-type carbide are finely regulated and controlled, and the TLP connection process is regulated according to the pre-welding structure of the two alloys, so that the problem of rapid precipitation of gamma' -phase in the welding process is solved, and 718Plus/Ni with uniform microstructure and good mechanical property is ensured to be obtained 3 The Al-based alloy TLP diffusion joint.
The beneficial effects of the invention are as follows:
(1) By adopting a method combining pre-welding heat treatment and Transient Liquid Phase (TLP) diffusion connection, the dissimilar gamma' -phase reinforced phase alloy 718Plus alloy and Ni are realized firstly 3 Diffusion bonding of Al-based alloys, 718Plus/Ni obtained 3 The Al-based alloy connecting joint has good microstructure and mechanical property;
(2) 718Plus and Ni 3 Al-based alloy has complex components and high alloying degree, and 718Plus alloy can generate gamma phase, eta phase, precipitation of TCP equal structures and distribution change and Ni in the heat treatment process 3 The present invention is directed to 718Plus alloy and Ni because of the occurrence of changes in the Al-based alloy in the duplex region (γ+γ '), eutectic region (γ - γ '), (γ+γ ')/(γ - γ ') interface region microstructure, γ ' phase, content, distribution, size, type of MC-type carbide 3 The problems of high gamma' -phase precipitation speed and large microstructure change of the Al-based alloy in the welding process are solved by a heat treatment process design (stress relief annealing, solid solution and aging treatment), and 718Plus alloy and Ni are accurately regulated and controlled 3 Microstructure of Al-based alloy before weldingEnsuring that 718Plus/Ni is completed under the condition that the welding part takes gamma' phase as main strengthening phase 3 High quality joining of Al-based alloys;
(3) For dissimilar gamma prime phase alloys (718 Plus alloy and Ni 3 Al-based alloy) has larger composition gap and is easy to generate diffusion void and other problems in the connecting process, and the invention is based on 718Plus alloy and Ni 3 The microstructure of the Al-based alloy before welding adjusts the TLP diffusion connection process such as connection temperature, heat preservation time, connection pressure and the like, controls the element interdiffusion behavior between the intermediate layer and the base material, reduces or even eliminates Cr-Mo-Ni-enriched boride formed in the TLP connection process on the premise of ensuring mechanical properties, inhibits the generation of defects such as holes, cracks and the like at the connection interface and ensures the connection quality of the joint.
(4) The invention reduces 718Plus/Ni by reasonably designing the pre-welding heat treatment process 3 The Al-based alloy TLP connection process has the requirements on connection temperature, connection pressure and heat preservation time, and improves production quality and efficiency.
(5) The invention fully utilizes the existing TLP connection process equipment, thus 718Plus/Ni can be obtained without increasing equipment investment and without increasing cost basically 3 The microstructure of the Al-based alloy welded joint has good quality and better mechanical properties at low temperature and high temperature, and the product competitiveness is enhanced.
In conclusion, the process can accurately control 718Plus alloy and Ni through pre-welding heat treatment 3 The microstructure of the Al-based alloy and the welding performance of the Al-based alloy are improved, and a proper TLP diffusion connection process is selected on the basis, so that the structure of the connection joint is more uniform, the formation of a hard alloy phase is reduced, the residual stress is reduced, and the high-temperature strength of the connection joint is improved. Wherein, the optimal tensile strength can reach 650-680 MPa, and the microhardness value is 410HV. 718Plus alloy and Ni obtained by the method 3 The normal temperature and high temperature mechanical properties of Al-based alloy dissimilar gamma' -phase metal joint are similar to those of Ni 3 Al-based alloy level.
Drawings
Fig. 1: 718Plus alloy and Ni in the present invention 3 Temperature and time in Al-based alloy TLP diffusion bonding processInter-control diagram.
Fig. 2: TLP connection joint microstructure map of example 1.
Fig. 3: TLP linker microstructure map of example 3.
Fig. 4: TLP connection joint microstructure map of example 4.
Fig. 5: TLP linker microstructure map of example 5.
Detailed Description
The present invention will be described in detail with reference to specific examples. The following examples will assist those skilled in the art in further understanding the present invention, but are not intended to limit the invention in any way.
The mass composition elements of the 718Plus alloy related by the invention are as follows: cr: 17.00-21.00, fe: 8.00-10.00, co:8.00 to 10.00, nb:5.20 to 5.80, mo:2.50 to 3.10, al:1.20 to 1.70, ti:0.50 to 1.00, B:0.003 to 0.008, C:0.01 to 0.05, P: 0.004-0.020, W:<1.40，Mn：<0.35，，Si：<0.035，S：<0.025, the balance being Ni, in mass percent; ni (Ni) 3 The Al-based superalloy alloy comprises the following mass composition elements; al:7.6 to 8.5, cr:7.4 to 8.2, mo:3.5 to 5.5, W:1.5 to 2.5, ti:0.6 to 1.2, hf:0.3 to 0.9, C:0.06 to 0.2, fe:<2，Si：<0.5，Mn：<0.5，B：<0.05, the balance being Ni, in mass percent.
Example 1:
step one, pretreatment:
ni was fed by wire cutting machine 3 The Al-based superalloy was cut into 25X 10X 3mm specimens, and the 718Plus alloy was cut into 15X 10X 3mm specimens.
Step two, stress relief annealing:
heating two box furnaces to 850 ℃ and 850 ℃ respectively, and after the temperature is stable, heating the Ni obtained in the first step 3 The Al-based superalloy and 718Plus alloy samples are placed into preheated corundum crucibles, the corundum crucibles with the samples are respectively placed into constant temperature areas of two box-type furnaces, the temperature is kept for 2 hours and 7 hours respectively, and the furnace is cooled to room temperature after the heat preservation is finished.
Step three, solution treatment:
heating the box furnace to 1160 ℃, and after the temperature is stable, filling Ni into the furnace obtained in the second step 3 Placing the corundum crucible of the Al-based superalloy sample into a constant temperature area of a box-type furnace, preserving the temperature of the sample in the box-type furnace for 9 hours, closing a heating program of the box-type furnace after the preservation is finished, and taking out the corundum crucible and the sample after the box-type furnace is cooled to room temperature. Heating the box-type furnace to 960 ℃, after the temperature is stable, placing the corundum crucible filled with the 718Plus alloy sample obtained in the second step into a constant temperature area of the box-type furnace, preserving the temperature of the sample in the box-type furnace for 3 hours, closing a heating program of the box-type furnace after the preservation is finished, and taking out the corundum crucible and the sample after the box-type furnace is cooled to room temperature.
Step four, aging treatment:
heating the box furnace to 950 ℃, and after the temperature is stable, filling Ni into the furnace obtained in the third step 3 Placing the corundum crucible of the Al-based superalloy sample into a constant temperature area of a box-type furnace, preserving heat of the sample in the box-type furnace for 9 hours, heating the box-type furnace to 1100 ℃ after the heat preservation is finished, preserving heat for 5 hours, closing a heating program of the box-type furnace after the heat preservation is finished, and taking out the corundum crucible and the sample after the box-type furnace is cooled to room temperature. Heating the box furnace to 700 ℃, after the temperature is stabilized, placing the corundum crucible filled with the 718Plus alloy sample obtained in the third step into a constant temperature area of the box furnace, preserving the temperature of the sample in the box furnace for 7 hours, heating the box furnace to 730 ℃ after the preservation is finished, preserving the temperature for 5 hours, closing a heating program of the box furnace after the preservation is finished, and taking out the corundum crucible and the sample after the box furnace is cooled to room temperature.
Step five, surface treatment:
mixing 718Plus alloy obtained in the fourth step with Ni 3 Sequentially polishing the welding surface of the Al-based superalloy by using 400# SiC abrasive paper, 600# SiC abrasive paper, 800# SiC abrasive paper, 1000# SiC abrasive paper and 1200# SiC abrasive paper, polishing by using a polishing machine, putting the two high-temperature alloys into a beaker filled with acetone, and putting the beaker into an ultrasonic cleaner for ultrasonic cleaning for 10 minutes; then washing the surface to be welded with alcohol, and drying with cold air for standby;
step six, preparing a TLP connection sample:
BNi-2 amorphous foil strips with the thickness of 50 mu m (BNi-2 is a known material, the composition of which is 7Cr-4.5Si-3.2B-3Fe and the balance of Ni.) are selected as an intermediate layer, the intermediate layer is pickled, cleaned by clear water to remove acid liquor, and then cleaned by alcohol or acetone and dried. Placing the treated BNi-2 interlayer in 718Plus alloy and Ni 3 Assembling the Al-based superalloy to form a TLP connection sample;
step seven, implementing a TLP connection process:
placing the TLP connection sample assembled in the sixth step into a vacuum diffusion furnace, applying 0.3MPa axial pressure, closing the furnace door and starting vacuumizing, when the vacuum degree of the vacuum diffusion furnace reaches 10 -2 ～10 -3 Heating is started when the Pa level is heated to 1120 ℃ (in the process of from room temperature to 500 ℃, the heating rate is controlled to be 5 ℃/min, the furnace temperature is controlled to be 500 ℃ for 20 minutes, the furnace temperature is uniform, in the process of from 500 ℃ to 900 ℃, the heating rate is controlled to be 3 ℃/min, the furnace temperature is uniform when the furnace temperature is 900 ℃, in the process of from 900 ℃ to 1120 ℃, the heating rate is controlled to be 2 ℃/min), after the temperature is stable, the diffusion connection is completed after the temperature is stable, the joint is formed, and the joint is cooled to the room temperature along with the furnace after the heat preservation is finished, and is taken out.
The obtained ATI718Plus alloy and Ni 3 The microstructure of the Al-based superalloy TLP connection joint and the welded joint is shown in FIG. 2. The tensile strength is 656MPa at most, the microhardness value is 458HV, the welded joint has good mechanical properties, and the element distribution is relatively uniform.
Example 2
This example differs from example 1 in that the two base metal alloys are not subjected to a stress relief annealing process, and in step three, ni is used 3 Heating Al-based superalloy in a box furnace to 1100 ℃, performing solution treatment for 7 hours, heating 718Plus alloy in the box furnace to 960 ℃, and performing solution treatment for 3 hours; and step seven, heating to 1040 ℃, preserving heat for 30 minutes to finish diffusion connection so as to form a joint, and cooling to room temperature along with a furnace after the heat preservation is finished and taking out.
The other steps are the same as in example 1.
Obtaining ATI718Plus alloy and Ni 3 Al-based superalloy TLP connection joint. The tensile strength is up to 410MPa, the microhardness value is 578HV, the obtained TLP diffusion joint has very low tensile strength and poor mechanical property, and elements in a joint area have obvious enrichment phenomenon in a certain area and have obvious defects such as air holes, cracks and the like.
Example 3
This example differs from example 1 in that Ni was added in step three 3 Heating Al-based superalloy to 1180deg.C in a box furnace, performing solution treatment for 5 hr, heating 718Plus alloy to 900 deg.C in the box furnace, and performing solution treatment for 4 hr; and step seven, heating to 1040 ℃, preserving heat for 45 minutes to finish diffusion connection so as to form a joint, and cooling to room temperature along with a furnace after the heat preservation is finished and taking out.
The other steps are the same as in example 1.
Obtaining ATI718Plus alloy and Ni 3 The microstructure of the Al-based superalloy TLP connection joint and the welded joint is shown in FIG. 3. The tensile strength is 541MPa at most, the microhardness value is 512HV, the joint structure and mechanical property of the obtained TLP diffusion joint are greatly improved compared with those of the example 2, the enrichment phenomenon of elements in a certain region in the joint region is weakened, and the defect degree of pores, cracks and the like is reduced.
Example 4
This example differs from example 1 in that Ni was added in step three 3 Heating Al-based superalloy in a box furnace to 1220 ℃ for 8 hours of solution treatment, heating 718Plus alloy in the box furnace to 1030 ℃ for 3 hours of solution treatment; and step seven, heating to 1080 ℃, applying a connection pressure of 1MPa to the TLP connection sample, preserving heat for 45 minutes to finish diffusion connection so as to form a joint, and cooling to room temperature along with a furnace after the heat preservation is finished, and taking out.
The other steps are the same as in example 1.
Obtaining ATI718Plus alloy and Ni 3 The microstructure of the Al-based superalloy TLP connection joint and the welded joint is shown in FIG. 4. Tensile strength is 664MPa at most, microhardness value is 432HV, and welded jointThe head has no enrichment of elements in a certain area and the weld joint has no defects such as cracks, air holes and the like.
Example 5
This example differs from example 1 in that Ni was added in step three 3 Heating Al-based superalloy in a box furnace to 1260 ℃ for 7 hours of solution treatment, heating 718Plus alloy in the box furnace to 1080 ℃ for 4 hours of solution treatment; in the fourth step, ni 3 Heating the Al-based superalloy sample in a box furnace to 980 ℃ for heat preservation for 9 hours, heating the box furnace to 1150 ℃ and heat preservation for 5 hours after heat preservation is finished, heating the 718Plus alloy sample in the box furnace to 720 ℃ for heat preservation for 9 hours, heating the box furnace to 750 ℃ and heat preservation for 6 hours after heat preservation is finished, heating to 1040 ℃ in the seventh step, applying a connecting pressure of 3MPa to the TLP connected sample, performing heat preservation for 1 hour to finish diffusion connection to form a joint, and cooling to room temperature along with the furnace after heat preservation is finished and taking out.
The other steps are the same as in example 1.
Obtaining ATI718Plus alloy and Ni 3 The microstructure of the Al-based superalloy TLP connection joint and the welded joint is shown in FIG. 5. The tensile strength is 680MPa at most, the microhardness value is 410HV, and the obtained TLP diffusion joint has higher tensile strength, and the joint is tightly combined and well formed.
Based on the above, the invention combines the pre-welding structure control of the parent metal and the TLP process design, and establishes 718Plus and Ni 3 The relation between the Al-based alloy pre-welding structure and the TLP process overcomes the problem of rapid separation of gamma' phase in the welding process, and realizes 718Plus and Ni 3 High quality connection between Al-based alloys.
The above-mentioned heterogeneous gamma prime phase strengthened superalloy transient liquid phase diffusion joining method, the equipment used is well known in the art, and the operating process used is well known to those skilled in the art.
The invention is not a matter of the known technology.

Claims (7)

1. The method for connecting the dissimilar gamma' -phase reinforced superalloy is characterized by comprising the following steps of:
step one, pretreatment: ni is added with 3 Processing Al-based alloy and 718Plus alloy to the required size;
step two, stress relief annealing is carried out to Ni 3 The Al-based alloy ingot is preserved for 1 to 6 hours at the temperature of 600 to 1000 ℃, and after the preservation is finished, the furnace is cooled to the room temperature; preserving the heat of the forged 718Plus blank for 1-10 hours at 500-1000 ℃, and cooling the blank to room temperature after the heat preservation is finished;
step three, solution treatment: preserving the heat of the 718Plus alloy obtained in the second step at 900-1200 ℃ for 2-10 hours, and cooling to room temperature after the heat preservation is finished; ni obtained in the second step 3 The Al-based alloy is subjected to heat preservation at 1100-1300 ℃ for 2-10 hours, and is cooled to room temperature after heat preservation is finished;
step four, aging treatment: ni obtained in the third step 3 The Al-based alloy is subjected to heat preservation at 900-1000 ℃ for 6-10 hours, then subjected to heat preservation at 1050-1150 ℃ for 4-6 hours, and cooled to room temperature after heat preservation; the 718Plus alloy in the third step is kept at 700-720 ℃ for 6-10 hours, then kept at 720-750 ℃ for 5-8 hours, and furnace cooled to room temperature after the heat preservation is finished;
step five, surface treatment: mixing 718Plus alloy obtained in the fourth step with Ni 3 Grinding and polishing the to-be-welded part of the Al-based alloy, then ultrasonically cleaning the to-be-welded part in acetone for 10-30 minutes, flushing the to-be-welded surface with alcohol, and drying with cold air for later use;
step six, preparing a TLP diffusion connection structure: the foil strip of the interlayer material and the two alloys obtained in the fifth step are respectively 718Plus alloy/interlayer/Ni according to the upper, middle and lower parts 3 Stacking Al-based alloy to obtain a TLP structure to be connected;
step seven, TLP diffusion connection: placing the TLP structure to be connected obtained in the sixth step in a vacuum diffusion furnace, applying 0.1-0.5 Mpa of axial pressure, closing a furnace door, and vacuumizing to a vacuum degree of 10 -2 ~10 -3 Pa; and then heating the vacuum diffusion furnace to 1000-1150 ℃, preserving heat for 5-120 minutes after reaching the temperature, or applying connection pressure to the TLP connection structure in the diffusion furnace for preserving heat for 5-120 minutes, and cooling to room temperature along with the furnace after the heat preservation is finished, so that the required product can be obtained.
2. The method for joining dissimilar gamma prime phase strengthened superalloys according to claim 1, wherein the joining pressure applied in the step seven is 0.2 to 3.0MPa.
3. The method for joining dissimilar gamma prime phase strengthened superalloys according to claim 1, wherein the cooling means in step three is furnace cooling, water cooling or air cooling.
4. The method for joining dissimilar gamma' -phase strengthened superalloys according to claim 1, wherein the polishing is performed by sequentially polishing the surface of the base material with 400#, 600#, 800#, 1000#, 1500#, 2000# abrasive papers, and the polishing is performed by modifying the surface of the base material with a diamond polishing paste.
5. The method for joining dissimilar gamma prime phase strengthened superalloys according to claim 1, wherein the interlayer material is BNi-2, BNi-3, BNi-9, or Mn-Ni-Cr interlayer alloy.
6. The method for connecting dissimilar gamma' -phase reinforced high-temperature alloy according to claim 1, wherein the alloy in the second to fourth steps is placed in a high-temperature resistant corundum crucible, the corundum crucible is preheated before use, the preheating temperature is 400-600 ℃, and the preheating time is 2-6 hours; the heat preservation process is carried out in a box-type resistance furnace.
7. The method for joining dissimilar gamma' -phase strengthened superalloys according to claim 1, wherein in the seventh step, the temperature rise process to the holding temperature is: the temperature rising rate from room temperature to 500 ℃ is 5-7 ℃/min, and the furnace temperature is kept for 20-30 minutes after reaching 500 ℃; 500. the temperature rising rate in the process of between the temperature and 900 ℃ is 3-4 ℃/min, and when the furnace temperature reaches 900 ℃, the temperature is kept for 15-30 minutes; the temperature rising rate from 900 ℃ to the target temperature is controlled to be 2-3 ℃/min, and the target temperature is reached.
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