CN112853154B - Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application - Google Patents

Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application Download PDF

Info

Publication number
CN112853154B
CN112853154B CN202110003684.0A CN202110003684A CN112853154B CN 112853154 B CN112853154 B CN 112853154B CN 202110003684 A CN202110003684 A CN 202110003684A CN 112853154 B CN112853154 B CN 112853154B
Authority
CN
China
Prior art keywords
intermediate layer
nickel
welding
alloy material
based intermediate
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
CN202110003684.0A
Other languages
Chinese (zh)
Other versions
CN112853154A (en
Inventor
刘凤美
李琪
易耀勇
高海涛
李丽坤
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
China Uzbekistan Welding Research Institute of Guangdong Academy of Sciences
Original Assignee
China Uzbekistan Welding Research Institute of Guangdong Academy of Sciences
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by China Uzbekistan Welding Research Institute of Guangdong Academy of Sciences filed Critical China Uzbekistan Welding Research Institute of Guangdong Academy of Sciences
Priority to CN202110003684.0A priority Critical patent/CN112853154B/en
Publication of CN112853154A publication Critical patent/CN112853154A/en
Application granted granted Critical
Publication of CN112853154B publication Critical patent/CN112853154B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/06—Metallic powder characterised by the shape of the particles
    • B22F1/065—Spherical particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • 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
    • B23K20/24—Preliminary treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/023—Alloys based on nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
    • F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
    • F01D5/12—Blades
    • F01D5/14—Form or construction
    • F01D5/18—Hollow blades, i.e. blades with cooling or heating channels or cavities; Heating, heat-insulating or cooling means on blades
    • F01D5/186—Film cooling
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01D—NON-POSITIVE DISPLACEMENT MACHINES OR ENGINES, e.g. STEAM TURBINES
    • F01D5/00—Blades; Blade-carrying members; Heating, heat-insulating, cooling or antivibration means on the blades or the members
    • F01D5/12—Blades
    • F01D5/28—Selecting particular materials; Particular measures relating thereto; Measures against erosion or corrosion
    • F01D5/282—Selecting composite materials, e.g. blades with reinforcing filaments

Abstract

The invention discloses a nickel-based intermediate layer alloy material, a preparation method thereof, a weldment, a welding method and application, and relates to the technical field of welding materials. The nickel-based interlayer alloy material comprises the following chemical components in percentage by weight: cr11.9-13.2%, Co6.5-7.8%, Mo0.5-1.7%, W4.1-5.2%, Al2.4-3.6%, Ti4.1-5.3%, Ta3.0-4.2%, Re 0-3.1%, Ru1.5-3.1%, B0.5-1.1%, Si 0.3-0.8% and the balance of nickel. The preparation method comprises the step of smelting metal and/or alloy into the nickel-based intermediate layer alloy material according to the chemical composition. The welding method comprises the step of welding a weldment by adopting the alloy material. And the weldment is obtained by welding by adopting the welding method. The high-temperature strength of the joint of the weldment obtained by welding the alloy material provided by the invention is high.

Description

Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application
Technical Field
The invention relates to the technical field of welding materials, in particular to a nickel-based intermediate layer alloy material, a preparation method thereof, a weldment, a welding method and application.
Background
Along with the continuous promotion of aeroengine performance, temperature is higher and higher before the turbine, and under the unchangeable condition of other conditions, every 100 ℃ (centigrade degrees) of temperature promotion before the turbofan engine turbine, the maximum thrust of this engine just can promote nearly 20%. Therefore, the operating temperature before the turbine is increased in competition in all countries, and as can be seen from fig. 1, the temperature before the turbine in China has a certain gap compared with the advanced countries in the world.
The turbine blade is required to have stronger high-temperature resistance when the temperature in front of the turbine of the engine is required to be increased, the most important measure is to improve the high-temperature resistance of the turbine blade material and the cooling technology of the turbine blade material, and as can be seen from figure 2, the intermetallic compound has higher high-temperature resistance, has the characteristics of high melting point, small density, good oxidation resistance, good corrosion resistance, high-temperature strength and the like, can be used as a key component material of an aeroengine, and has wide application prospects. The application aims at the Ni with wide application prospect3And welding the Al intermetallic compound high-temperature alloy.
The turbine blade at the high temperature end of the engine (as shown in figure 3) is a complex cavity structure, and the cavity is used for cooling the blade. The manufacturing process is finish machining after casting, the manufacturing and machining difficulty is very high, unequal gaps are easily caused in the machining and the assembly process of the tenon and the blade body, the maximum gap can reach 0.08mm, and the welding is difficult.
The transient liquid phase diffusion welding is one kind of diffusion welding, and its welding schematic diagram is shown in fig. 4, and it usually uses material with lower melting point than that of the base material as intermediate layer, when it is heated to connection temperature, the intermediate layer is melted, and the transient liquid film is formed on the joint surface, and in the course of heat-insulating, the thickness of the liquid film is reduced and disappears along with the diffusion of low-melting point component to the base material, and then the heat-insulating is implemented for a certain time to make the components uniform, and finally the welding seam joint with uniform structure is formed. From fig. 4 we can see that the wider the weld, the more difficult it is for the elements of the interlayer material to diffuse, so that the large gap greatly increases the difficulty of welding the aeroengine blade.
At present Ni3The welding of Al high-temperature alloy adopts transient liquid phase diffusion welding, and the most part of Ni-based intermediate layer material is Ni3Al base material component is used as a matrix, and a small-atom-radius element boron is added as a melting reduction element in the diffusion welding processAnd B element diffuses to the base metal to realize isothermal solidification of the welding joint and finish welding. But the intermediate layer material can only meet the welding of small gaps (the assembly gap is less than 0.03mm), the high-temperature (1100 ℃) tensile strength of the joint reaches 80-85% of that of the parent metal, the high-temperature (1100 ℃) lasting (100 h) strength of the joint reaches 90% of that of the parent metal, and the application requirement of an aeroengine is met. However, when the gap of the welding seam is large (more than 0.03mm), the diffusion degree of the B element is limited, so that a low-melting-point phase still exists in the welding seam, the strength of the joint is greatly reduced at high temperature and lasting (1100 ℃ and 100h), and the application requirement of an aeroengine cannot be met.
However, in practical production application, due to the complexity of the structure, in the process of machining and assembling, the assembling clearance of one workpiece is not equal, and sometimes the assembling clearance is larger than 0.03mm and even reaches 0.08 mm. If the clearance is strictly controlled, the processing difficulty is very high, the processing period is very long, the rejection rate is very high, and the cost is high, so that the method cannot be imagined. Thus solving Ni3The unequal-gap welding of the Al high-temperature alloy improves the high-temperature durable (1100 ℃, 100h) strength of the joint, and is a priority.
In view of this, the invention is particularly proposed.
Disclosure of Invention
The invention aims to provide a nickel-based intermediate layer alloy material, a preparation method thereof, a weldment, a welding method and application.
The invention is realized by the following steps:
in a first aspect, an embodiment of the present invention provides a nickel-based intermediate layer alloy material, which comprises, by weight: 11.9 to 13.2% of Cr, 6.5 to 7.8% of Co, 0.5 to 1.7% of Mo, 4.1 to 5.2% of W, 2.4 to 3.6% of Al, 4.1 to 5.3% of Ti, 3.0 to 4.2% of Ta, 0 to 3.1% of Re, 1.5 to 3.1% of Ru, 0.5 to 1.1% of B, 0.3 to 0.8% of Si and the balance of Ni.
In an alternative embodiment, the nickel-based interlayer alloy material is in the form of powder or a strip;
in an alternative embodiment, when the nickel-based intermediate layer alloy material is in a powder shape, the particle size is-200 meshes to +800 meshes;
in an alternative embodiment, the nickel-based intermediate layer alloy material is in the form of a ribbon, and has a thickness of 10um to 100 um.
In a second aspect, an embodiment of the present invention provides a method for preparing a nickel-based intermediate layer alloy material, for preparing the nickel-based intermediate layer alloy material provided by the embodiment of the present invention, including:
and (3) mixing and smelting corresponding metal and/or alloy into alloy according to the chemical composition of the alloy material.
In an alternative embodiment, the method further comprises: screening the alloy obtained after smelting to obtain alloy powder with the grain size of-200 meshes to +800 meshes;
in an alternative embodiment, the sieving means is ultrasonic sieving.
In an alternative embodiment, the melting process is carried out under a vacuum inert gas atmosphere.
In an alternative embodiment, the alloy obtained after smelting is made into a strip with the thickness of 10um-100 um;
in an alternative embodiment, the alloy obtained after melting is formed into a strip by a rapid quenching process.
In a third aspect, an embodiment of the present invention provides a welding method, including: the nickel-based intermediate layer alloy material provided by the embodiment of the invention is used as an intermediate layer, and the Ni is welded by adopting transient liquid phase diffusion welding3An Al alloy base material.
In an alternative embodiment, the welding parameters are: the temperature is 1190-1210 ℃, the pressure is 0.3-6MPa, and the heat preservation time is 5-7 h.
In a fourth aspect, an embodiment of the present invention provides a weldment obtained by welding using the welding method provided in the embodiment of the present invention.
In a fifth aspect, embodiments of the present invention provide the use of the weldment described above in an engine.
The invention has the following beneficial effects:
adding boron and silicon into the alloy together, so that silicon replaces part of boron, the content of boron in the alloy is reduced, and the effects of improving the lasting plasticity and the lasting time of the joint are achieved; ruthenium (Ru) is added into the alloy, so that the high-temperature durability of the joint is improved; increasing Ti in the alloyThe element content can achieve the effect of improving the high-temperature strength of the joint. Controlling the added elements within a reasonable content range, and enabling the elements to mutually cooperate, so that the alloy material is welded with Ni under the condition of unequal gaps (the assembly gap is more than or equal to 0.03mm)3The Al high-temperature alloy has the advantages that the joint is high-temperature durable (1100 ℃, 100h), the strength reaches more than 90 percent of that of a base material, and the performance of the joint is equivalent to or better than that of a welded joint with a small gap (the assembly gap is less than 0.03 mm).
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are required for the present application will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and that for those skilled in the art, other related drawings can be obtained from these drawings without inventive effort.
FIG. 1 is a graph comparing pre-turbine operating temperatures;
FIG. 2 is a high temperature diagram of a superalloy;
FIG. 3 is a schematic view of an aircraft engine turbine blade configuration;
FIG. 4 is a schematic diagram of transient liquid phase diffusion bonding (TLP bonding);
FIG. 5 is a microscopic structure view of a powdery nickel base interlayer material obtained in example 1;
FIG. 6 is a schematic view of a strip-shaped nickel-based interlayer material obtained in example 1;
FIG. 7 is a schematic view of a weld butt test assembly drawing and a high temperature tensile specimen model;
FIG. 8 is a joint microstructure of a weld of example 1;
FIG. 9 shows the microstructure of the joint of the weld of example 1.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The nickel-based intermediate layer alloy material provided by the embodiment of the invention, the preparation method thereof, the weldment, the welding method and the application are specifically described below.
The nickel-based intermediate layer alloy material provided by the embodiment of the invention comprises the following chemical components in percentage by weight: 11.9 to 13.2% of Cr, 6.5 to 7.8% of Co, 0.5 to 1.7% of Mo, 4.1 to 5.2% of W, 2.4 to 3.6% of Al, 4.1 to 5.3% of Ti, 3.0 to 4.2% of Ta, 0 to 3.1% of Re, 1.5 to 3.1% of Ru, 0.5 to 1.1% of B, 0.3 to 0.8% of Si and the balance of Ni.
The nickel-based intermediate layer alloy material provided by the embodiment of the invention has the following characteristics:
1, B, Si, which can improve the durability of joint.
B is a typical melting point reducing element, a low-melting point nickel boron compound is formed in the intermediate layer material to achieve the purpose of melting point reduction, and meanwhile, B is a small-atom-radius element and is easy to diffuse to a base material to achieve the effect of isothermal solidification. When the mass fraction of B is increased to about 3.92%, a eutectic point is reached, at which the melting point is 1093 ℃, and the structure is composed of Ni and Ni3B, the component B. However, if the amount of B added to the nickel-base alloy is too large, it forms a brittle compound with Ni, which deteriorates the tensile strength and corrosion resistance of the joint, and therefore, it is necessary to control the amount of B in the intermediate layer.
Si is also a typical melting point depressant, and as can be seen from Table 1, Si is in Ni3The Al crystal lattice also has a certain diffusion barrier and diffusion coefficient, and meanwhile, silicon is partially gathered in a crystal boundary to generate a fine granular secondary phase, so that the generation of crystal boundary sliding and cracks is prevented, and the lasting plasticity and the lasting time of the joint are favorably improved.
In the application, Si which can be diffused and has the melting reducing effect is used for replacing part of B elements, so that the melting temperature of the intermediate layer material can be reduced, and the durability of the joint can be improved.
TABLE 1 atom 1B, Si in Ni3Atomic diffusion parameter in Al lattice
Figure BDA0002882728200000061
2. Adding solute element ruthenium (Ru) to improve the high-temperature durability of the joint
Ruthenium is a platinum group metal, and has stable property and strong corrosion resistance. Ru is added into the intermediate layer, the distribution ratio of each element in the gamma/gamma' two phases is reduced, the homogenization degree of alloy elements is favorably improved, and the tendency of forming harmful TCP phases by the alloy is reduced. Ru is a very weak positive segregation element, the distribution ratio of Ru in gamma/gamma 'is about 0.7, and the Ru is mainly distributed in the gamma phase and has larger atomic radius than Ni, so that the mismatching degree of gamma/gamma' is increased towards the secondary direction, raft tissues are easier to obtain in the alloy, and the alloy with high raft tendency usually has high service life at the high temperature of 1100 ℃. Therefore, the addition of Ru can obviously improve the high-temperature durability of the welding seam.
3. Increase the content of Ti element and improve the high-temperature strength of the joint
Ti forms an ordered face-centered cubic intermetallic compound-Ni in the intermediate layer material3Ti plays a role in precipitation strengthening, and the content of Ti is increased, so that the tendency of Mo, Cr, Re and other elements to be segregated in a gamma phase is increased; under a certain Al content, the number of gamma' phase is increased along with the increase of Ti content, and the high-temperature strength and the high-temperature corrosion resistance of the alloy are improved.
4. In a preferred embodiment, the solute element rhenium (Re) is added to improve the high temperature strength of the joint.
Re is mainly distributed in a gamma matrix to form a short-range ordered atomic group, the atomic group can effectively prevent dislocation movement, inhibit coarsening of a gamma' phase, play a good solid solution strengthening effect and obviously improve the creep property of an intermediate layer material, thereby improving the high-temperature strength and the oxidation resistance of a welding line. However, Re is segregated to dendrite, difficult to diffuse, difficult to homogenize during high-temperature solution treatment, and harmful TCP phase is precipitated during long-term use, which damages the high-temperature durability of the weld, so that the addition content of Re is controlled.
5. Calculating liquidus temperature and electron vacancy number by using element average concentration
Figure BDA0002882728200000071
Figure BDA0002882728200000072
The liquidus temperature of the intermediate layer material of the invention is calculated to be 1138 ℃, the electron vacancy number NV is 2.371, the alloy liquidus is suitable, the electron vacancy number is less than 2.45, the alloy structure is stable, and the TCP phase is not separated out.
Therefore, the nickel-based intermediate layer alloy material provided by the embodiment of the invention has reasonable proportion of the added elements, and the elements are mutually matched, so that the alloy material can be used for welding the Ni3Al high-temperature alloy under the condition of unequal gaps (the assembly gap is greater than or equal to 0.03mm), the joint is durable at high temperature (1100 ℃, 100h), the strength can reach more than 90% of that of the base material, and the performance of the welded joint is equivalent to or better than that of a welded joint with a small gap (the assembly gap is less than 0.03 mm).
Preferably, the nickel-based intermediate layer alloy material is in a powder or strip shape for convenient welding.
More preferably, when the nickel-based intermediate layer alloy material is powdery, the grain diameter is-200 meshes to +800 meshes; when the nickel-based intermediate layer alloy material is in a strip shape, the thickness is 10-100 um.
The embodiment of the invention provides a preparation method of a nickel-based intermediate layer alloy material, which is used for preparing the nickel-based intermediate layer alloy material provided by the embodiment of the invention and comprises the following steps:
and (3) mixing and smelting corresponding metal and/or alloy into alloy according to the chemical composition of the alloy material.
The method comprises the following steps:
s1, putting the corresponding simple metal or a part of simple metal and a part of intermediate alloy or a plurality of intermediate alloys into a smelting furnace to smelt and form ingots according to the chemical components of the alloy material to be prepared.
Preferably, in order to ensure the purity of the prepared alloy material, the smelting process is carried out under a vacuum inert gas atmosphere.
S2, carrying out ultrasonic screening on the alloy ingot obtained after smelting to obtain alloy powder of-200 meshes to +800 meshes; or the smelted alloy ingot is made into a strip with the thickness of 10-100 um by adopting a quick quenching process.
The welding method provided by the embodiment of the invention comprises the following steps: the nickel-based intermediate layer alloy material provided by the embodiment of the invention is used as an intermediate layer, and the Ni is welded by adopting transient liquid phase diffusion welding3An Al alloy base material.
In the welding method provided by the embodiment of the invention, the alloy material provided by the invention is used as the interlayer for welding, so that Ni is welded under the condition of unequal gaps (the assembly gap is more than or equal to 0.03mm)3The high-temperature endurance strength of the Al high-temperature alloy welding seam is high, and the qualified rate of welded parts is high.
Preferably, to ensure that a weldment with better performance can be obtained, welding parameters during welding are as follows: the temperature is 1190-1210 ℃, the pressure is 0.3-6Mpa, and the heat preservation time is 5-7 h.
Preferably, in order to further ensure that a weldment with better performance can be obtained, the welding process further comprises a heat treatment process, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
The weldment provided by the embodiment of the invention is obtained by welding by the welding method provided by the invention, so that the weldment has better quality; the engine can be applied to the engine.
The features and properties of the present invention are described in further detail below with reference to examples.
Example 1
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 4.7% of Ti, 3.6% of Ta, 1.6% of Re, 2.3% of Ru, 0.8% of B, 0.6% of Si and 57.9% of Ni.
The preparation method of the alloy material comprises the following steps: mixing Ni, Cr, Co, Mo, W, Al, Ti, Ta, Re, Ru, NiB alloy and Si according to the above-mentioned mass percentage, adopting vacuum smelting inert gas, adopting ultrasonic screening to obtain the spherical powder whose grain size is-200- +800 meshes.
And calculating that the liquidus temperature of the intermediate layer material is 1138 ℃, the electron vacancy number NV is 2.371, the electron vacancy number is less than 2.45, the alloy structure is stable, and a TCP phase is not precipitated.
A welding method specifically comprises the following steps:
welding Ni with the prepared powdery nickel-based interlayer material3The Al high-temperature alloy IC10 has the welding technological parameters as follows: setting the welding temperature parameter to 1200 ℃, setting the pressure parameter to 5MPa, setting the heat preservation time parameter to 6 hours, setting the welding initial gap to be about 0.03-0.08 mm, and cooling along with the furnace after welding.
And then carrying out postweld heat treatment on the welded joint, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
Example 2
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 4.7% of Ti, 3.6% of Ta, 3.1% of Ru, 0.5% of B, 0.8% of Si and 58.8% of Ni.
The preparation method of the alloy material comprises the following steps: mixing Ni, Cr, Co, Mo, W, Al, Ti, Ta, Re, Ru, NiB alloy and Si in proportion, smelting inert gas in vacuum, and ultrasonically screening to obtain spherical powder with the granularity of-200 +800 meshes.
And calculating the temperature of the liquid phase line of the intermediate layer material to be 1152 ℃, the electronic space number NV to be 2.251, the electronic space number to be less than 2.45, the alloy structure to be stable and no TCP phase to be separated out.
A welding method specifically comprises the following steps:
welding Ni with the prepared powdery nickel-based interlayer material3The Al high-temperature alloy IC10 has the welding technological parameters as follows: setting the welding temperature parameter to 1210 ℃, setting the pressure parameter to 5MPa, setting the heat preservation time parameter to 6 hours, setting the welding initial gap to be about 0.03-0.08 mm, and cooling along with the furnace after welding.
And then carrying out postweld heat treatment on the welded joint, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
Example 3
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 4.7% of Ti, 3.6% of Ta, 3.1% of Re3, 3.1% of Ru, 1.1% of B, 0.3% of Si and 55.6% of Ni.
The preparation method of the alloy material comprises the following steps: mixing Ni, Cr, Co, Mo, W, Al, Ti, Ta, Re, Ru, B and Si in proportion, adopting vacuum melting ingot making process, adopting quick quenching process to make the intermediate layer material into strip material whose thickness is 40 micrometers.
And calculating that the temperature of the liquid phase line of the intermediate layer material is 1140 ℃, the electron vacancy number NV is 2.437, the electron vacancy number is less than 2.45, the alloy structure is stable, and a TCP phase is not precipitated.
A welding method specifically comprises the following steps:
welding Ni3Al superalloy IC10 by using the prepared strip nickel-based interlayer material, wherein the welding process parameters are as follows: setting the welding temperature parameter to 1190 ℃, setting the pressure parameter to 5MPa, setting the heat preservation time parameter to 6 hours, setting the welding initial gap to be about 0.03-0.08 mm, and cooling along with the furnace after welding.
And then carrying out postweld heat treatment on the welded joint, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
Comparative example 1
This comparative example is substantially the same as example 1 except that silicon was completely replaced with an equal amount of boron.
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 4.7% of Ti, 3.6% of Ta, 1.6% of Re, 2.3% of Ru, 1.4% of Si and 57.9% of Ni.
The liquidus temperature of the intermediate layer material is calculated to be 1211 ℃, and the liquidus temperature exceeds the welding temperature of 1200 ℃ of the Ni3Al superalloy IC10, which shows that the temperature is not reduced enough by using Si alone as the melting-reducing element.
Comparative example 2
This comparative example is substantially the same as example 1 except that boron was completely replaced with an equal amount of silicon.
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 4.7% of Ti, 3.6% of Ta, 1.6% of Re, 2.3% of Ru, 1.4% of B and 57.9% of Ni.
The preparation method of the alloy material comprises the following steps: mixing Ni, Cr, Co, Mo, W, Al, Ti, Ta, Re, Ru and NiB alloy according to the above-mentioned mass percentage, adopting vacuum smelting inert gas and adopting ultrasonic screening process to obtain the spherical powder whose grain size is-200- +800 meshes.
And calculating the liquidus temperature of the intermediate layer material to be 1103 ℃, the electronic space number NV to be 2.370, the electronic space number to be less than 2.45, the alloy structure to be stable and no TCP phase to be separated out.
A welding method specifically comprises the following steps:
welding Ni with the prepared powdery nickel-based interlayer material3The Al high-temperature alloy IC10 has the welding technological parameters as follows: setting the welding temperature parameter to 1200 ℃, setting the pressure parameter to 5MPa, setting the heat preservation time parameter to 6 hours, setting the welding initial gap to be about 0.03-0.08 mm, and cooling along with the furnace after welding.
And then carrying out postweld heat treatment on the welded joint, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
Comparative example 3
This comparative example is essentially the same as example 1 except that the element ruthenium (Ru) was not added.
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 4.7% of Ti, 3.6% of Ta, 1.6% of Re, 0.8% of B, 0.6% of Si and 60.2% of Ni.
The preparation method of the alloy material comprises the following steps: mixing Ni, Cr, Co, Mo, W, Al, Ti, Ta, Re, NiB alloy and Si according to the above-mentioned mass percentage, adopting vacuum smelting inert gas, adopting ultrasonic screening to obtain spherical powder whose grain size is-200- +800 meshes.
And calculating that the temperature of the liquid phase line of the intermediate layer material is 1138 ℃, the electron vacancy number NV is 2.512, the electron vacancy number is more than 2.45, and the TCP phase can be separated out from the alloy structure.
A welding method specifically comprises the following steps:
welding Ni with the prepared powdery nickel-based interlayer material3The Al high-temperature alloy IC10 has the welding technological parameters as follows: setting the welding temperature parameter to 1200 ℃, setting the pressure parameter to 5MPa, setting the heat preservation time parameter to 6 hours, setting the welding initial gap to be about 0.03-0.08 mm, and cooling along with the furnace after welding.
And then carrying out postweld heat treatment on the welded joint, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
Comparative example 4
This comparative example is essentially the same as example 1 except that the element titanium (Ti) was not added.
A nickel-based intermediate layer alloy material comprises the following components in percentage by weight: 12.5% of Cr, 7.2% of Co, 1.1% of Mo, 4.7% of W, 3.0% of Al, 3.6% of Ta, 1.6% of Re, 2.3% of Ru, 0.8% of B, 0.6% of Si and 62.6% of Ni.
The preparation method of the alloy material comprises the following steps: mixing Ni, Cr, Co, Mo, W, Al, Ta, Re, Ru, NiB alloy and Si according to the above-mentioned mass percentage, adopting vacuum smelting inert gas, adopting ultrasonic screening process to obtain spherical powder whose grain size is-200- +800 meshes.
And calculating that the temperature of the liquid phase line of the intermediate layer material is 1139 ℃, the electron vacancy number NV is 2.372, the electron vacancy number is less than 2.45, the alloy structure is stable, and a TCP phase is not precipitated.
A welding method specifically comprises the following steps:
welding Ni with the prepared powdery nickel-based interlayer material3The Al high-temperature alloy IC10 has the welding technological parameters as follows: setting the welding temperature parameter as 1200 ℃, the pressure parameter as 5MPa and the heat preservation time parameter as 6 hours, and weldingAnd (4) cooling the welding head along with the furnace after the welding is finished, wherein the initial gap is about 0.03-0.08 mm.
And then carrying out postweld heat treatment on the welded joint, wherein the heat treatment process comprises the following steps: pretreatment is carried out at 1180 ℃ for multiplied by 2h, solid solution treatment is carried out at 1265 ℃ for multiplied by 2h/AC, and aging treatment is carried out at 1050 ℃ for multiplied by 4 h/AC.
Experimental example 1
As shown in FIG. 7, the specimens obtained by welding the examples 1 to 3 and the comparative examples 1 to 4 were subjected to a high temperature endurance test at 1100 ℃ and 36MPa and a high temperature elongation test at 1100 ℃ and the same specimen made of the base Ni3Al superalloy IC10 was used as a control group. The duration and high temperature tensile strength of each experimental group are recorded to table 1.
TABLE 1 high temperature Performance of welded joints in each experimental group
Figure BDA0002882728200000141
According to the table, the high-temperature strength of the welding joint of the weldment obtained by welding the alloy material provided by the embodiments of the invention is as high as more than 80% of the base material, and the lasting time of the joint can reach more than 90% of the base material. Comparing the example 1 with the comparative example 2, the high-temperature endurance performance of the comparative example 2 is lower than that of the example 1, which shows that the endurance performance of the welding joint can be improved by replacing a part of boron with silicon; comparing comparative example 3 with example 1, it is found that the high temperature durability of comparative example 3 is significantly lower than that of example 1, which shows that the high temperature durability can be significantly improved when ruthenium is added to the alloy material; comparing comparative example 4 with example 1, it can be seen that the high temperature strength of comparative example 4 is significantly lower than that of example 1, and the endurance performance is also reduced, which indicates that the high temperature strength of the joint can be significantly improved when titanium is added to the alloy material.
Experimental example 2
The microstructure of the weld joint obtained by welding in example 1 was observed. As shown in fig. 8 and 9, it can be seen that there is no distinct boundary between the weld and the base material, the weld forms γ and γ 'substantially identical to the base material, a "sunflower" -like (γ + γ') eutectic phase is distributed between the dendrites, and carbides and borides rich in Hf and Ta are partially precipitated in the middle of the weld, and no TCP phase is precipitated. The embodiment 1 is good in welding effect and obtains a good weld joint structure.
In summary, according to the nickel-based intermediate layer alloy material and the preparation method thereof provided by the invention, due to the reasonable configuration of the component contents of the elements and the mutual cooperation of the elements, Ni is welded on the alloy material under the condition of unequal gaps (the assembly gap is greater than or equal to 0.03mm)3The high-temperature Al alloy has the joint high-temperature durable strength (1100 ℃, 100h) reaching more than 90 percent of that of the parent metal, and has equivalent or better performance than that of a small-gap (the assembly gap is less than 0.03mm) welding joint.
In the welding method provided by the invention, the nickel-based intermediate layer alloy material provided by the embodiment of the invention is used as the intermediate layer, and the transient liquid phase diffusion welding is adopted to weld Ni3An Al alloy base material. Welding Ni under the condition of unequal gaps (the assembly gap is more than or equal to 0.03mm)3The high-temperature endurance strength of the Al high-temperature alloy welding seam is high, and the qualified rate of welded parts is high.
The weldment provided by the invention is obtained by welding by the welding method provided by the invention, so that the weldment has better quality; the engine can be applied to the engine.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.

Claims (14)

1. The nickel-based intermediate layer alloy material is characterized by comprising the following chemical components in percentage by weight: 11.9 to 13.2% of Cr, 6.5 to 7.8% of Co, 0.5 to 1.7% of Mo, 4.1 to 5.2% of W, 2.4 to 3.6% of Al, 4.1 to 5.3% of Ti, 3.0 to 4.2% of Ta, 0 to 3.1% of Re, 1.5 to 3.1% of Ru, 0.5 to 1.1% of B, 0.3 to 0.8% of Si and the balance of Ni.
2. The nickel-based intermediate layer alloy material according to claim 1, characterized in that the form of the nickel-based intermediate layer alloy material is powder or ribbon.
3. The nickel-based intermediate layer alloy material according to claim 2, wherein when the nickel-based intermediate layer alloy material is in a powdery form, the particle size thereof is-200 mesh to +800 mesh.
4. The nickel-based intermediate layer alloy material according to claim 3, wherein the thickness of the nickel-based intermediate layer alloy material is 10-100 um when it is in a strip shape.
5. A preparation method of the nickel-based intermediate layer alloy material is characterized by comprising the following steps of:
and (3) mixing and smelting corresponding metals and/or alloys into alloys according to the chemical components of the alloy materials.
6. The method for preparing the nickel-based intermediate layer alloy material according to claim 5, further comprising:
and screening the alloy obtained after smelting to obtain alloy powder with the grain size of-200 meshes to +800 meshes.
7. The method for preparing the nickel-based intermediate layer alloy material according to claim 6, wherein the screening manner is ultrasonic screening.
8. The method of claim 5, wherein the melting process is performed under a vacuum inert gas atmosphere.
9. The method for preparing the nickel-based intermediate layer alloy material according to claim 5, wherein the alloy obtained after melting is made into a strip with the thickness of 10um-100 um.
10. The method for preparing the nickel-based intermediate layer alloy material according to claim 9, wherein the alloy obtained after smelting is made into a strip by a rapid quenching process.
11. A method of welding, comprising: the nickel-based intermediate layer alloy material as claimed in any one of claims 1 to 4 is used as an intermediate layer, and Ni is welded by adopting transient liquid phase diffusion welding3An Al alloy base material.
12. Welding method according to claim 11, characterized in that the welding parameters are: the temperature is 1190-1210 ℃, the pressure is 0.3-6MPa, and the heat preservation time is 5-7 h.
13. A weldment obtained by welding using the welding method according to claim 11 or 12.
14. Use of a weldment as claimed in claim 13 in an engine.
CN202110003684.0A 2021-01-04 2021-01-04 Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application Active CN112853154B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202110003684.0A CN112853154B (en) 2021-01-04 2021-01-04 Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202110003684.0A CN112853154B (en) 2021-01-04 2021-01-04 Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application

Publications (2)

Publication Number Publication Date
CN112853154A CN112853154A (en) 2021-05-28
CN112853154B true CN112853154B (en) 2022-02-22

Family

ID=76001364

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202110003684.0A Active CN112853154B (en) 2021-01-04 2021-01-04 Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application

Country Status (1)

Country Link
CN (1) CN112853154B (en)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN113732479B (en) * 2021-08-11 2022-11-18 北京机电研究所有限公司 Dissimilar metal diffusion bonding method for G115 heat-resistant steel and Inconel740 high-temperature alloy
CN113736984B (en) * 2021-09-07 2022-06-28 北京航空航天大学 Ni3Post-treatment method for welded Al-based single crystal alloy
CN114147385B (en) * 2021-11-26 2023-03-14 西安理工大学 Welding wire for CMT fusion welding butt joint of copper-steel composite plate and preparation and welding method
CN114378477B (en) * 2022-03-08 2024-04-02 广东省科学院中乌焊接研究所 Mixed powder solder and preparation method thereof, welding interlayer and welding method

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3272247D1 (en) * 1981-04-08 1986-09-04 Johnson Matthey Plc Nickel alloys containing large amounts of chromium
EP0648850B1 (en) * 1993-09-20 1997-08-13 Mitsubishi Materials Corporation Nickel-based alloy
EP1536026A1 (en) * 2003-11-27 2005-06-01 Siemens Aktiengesellschaft High temperature resistant article
EP1914327A1 (en) * 2006-10-17 2008-04-23 Siemens Aktiengesellschaft Nickel-base superalloy
EP2420584B1 (en) * 2009-04-17 2013-06-19 IHI Corporation Nickel-based single crystal superalloy and turbine blade incorporating this superalloy
EP2597167B1 (en) * 2011-11-24 2014-04-23 Siemens Aktiengesellschaft DS superalloy and component
CN102628127A (en) * 2012-05-03 2012-08-08 丹阳恒庆复合材料科技有限公司 High-strength corrosion-resisting nickel base alloy and manufacturing method thereof

Also Published As

Publication number Publication date
CN112853154A (en) 2021-05-28

Similar Documents

Publication Publication Date Title
CN112853154B (en) Nickel-based intermediate layer alloy material, preparation method thereof, weldment, welding method and application
EP1842934B1 (en) Heat-resistant superalloy
US7165325B2 (en) Welding material, gas turbine blade or nozzle and a method of repairing a gas turbine blade or nozzle
JP5201708B2 (en) Ni-based heat-resistant alloy welding wire
EP2975145B1 (en) Heat-resistant ni-based alloy and method for manufacturing same
EP2902516B1 (en) A weld filler for nickel-base superalloys
EP3647442B1 (en) High gamma prime nickel based superalloy, its use, and method of manufacturing of turbine engine components
EP2383356A1 (en) Cobalt-Nickel Superalloys, and Related Articles
KR101832654B1 (en) Ni-Ir-BASED HEAT-RESISTANT ALLOY AND PROCESS FOR PRODUCING SAME
EP3815816B1 (en) High gamma prime nickel based superalloy, its use, turbine components and method of manufacturing thereof
TWI675110B (en) Ni-based heat-resistant alloy
JP7450639B2 (en) Low stacking fault energy superalloys, structural members and their uses
CN108838578B (en) Powder interlayer for TLP diffusion welding and welding method thereof
CN113941798A (en) Nickel-based alloy brazing material for high-temperature structural material and application thereof
JPH0116292B2 (en)
CN105458548A (en) Brazing material of high temperature alloy thin-walled structure and preparation method and application of brazing material
US4717435A (en) Gamma-prime precipitation hardening nickel-base yttria particle-dispersion-strengthened superalloy
Xie et al. Microstructural evolution and mechanical properties of Ni-based superalloy joints brazed using a ternary Ni-WB amorphous brazing filler metal
CN115449659A (en) Oxide dispersion strengthening nickel-based high-temperature alloy and preparation method and application thereof
TWI675109B (en) Ni-based heat-resistant alloy
CN116551244B (en) Au-containing low-melting-point nickel-based alloy, brazing filler metal and preparation method and application thereof
Che et al. Wettability of GH4099 and MHC alloys by AgCuTi, TiZrCuTi and NiCrSiB filler metals and evaluation of diffusion-brazability
US11759877B2 (en) Amorphous ductile braze alloy compositions, and related methods and articles
CN114632990B (en) Repair process for repairing defects of high-temperature alloy blade
CN115058624B (en) Nickel-based superalloy suitable for additive manufacturing

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant