Amorphous foil tape middle layer for TLP diffusion welding and application of amorphous foil tape middle layer

Abstract

The invention relates to the technical field of TLP diffusion welding, and discloses an amorphous foil strip middle layer for TLP diffusion welding and application thereof.The amorphous foil strip middle layer for TLP diffusion welding comprises, by mass, 17.3%-18.7% of Cr, 4.7%-6.3% of W, 2.8%-4.3% of B, 0.37%-0.43% of Ta, 4.7%-6.3% of Co, 0-0.1% of La and the balance Ni. The amorphous foil strip middle layer is used for welding cobalt-based high-temperature alloy, and the amorphous foil strip middle layer for TLP diffusion welding can be applied to welding of cobalt-based high-temperature alloy. Therefore, the cobalt-based high-temperature alloy welding joint with high strength and high welding rate can be obtained.

Description

Technical Field

[0001] The invention relates to the technical field of TLP diffusion welding, in particular to an amorphous foil intermediate layer for TLP diffusion welding and application thereof. Background Art

[0002] As the domestic aviation industry places increasingly higher demands on the manufacturing accuracy and service capability of welded structural parts, higher requirements are placed on the performance of high-temperature alloy welds. Transient liquid phase diffusion welding (TLP) is a welding technology, a type of diffusion welding. TLP diffusion welding technology is to add an intermediate layer alloy material containing a melting-reducing element between the base materials to be welded. During the heating process, the intermediate layer alloy melts to form a transient liquid phase, and then forms a welded joint through isothermal solidification and composition homogenization. Compared with traditional welding methods, the advantage of using TLP diffusion welding for high-temperature alloys is that the welding deformation is small and it is easy to achieve high-precision welding of complex structural parts. The selection of a suitable intermediate layer alloy is crucial to the quality of the TLP diffusion welded joint. However, the tensile strength and welding rate of the joints welded with the intermediate layer alloy in the existing high-temperature alloy TLP diffusion welding process are relatively low. Summary of the invention

[0003] In view of this, the present invention provides an amorphous foil intermediate layer for TLP diffusion welding, and uses the amorphous foil intermediate layer for welding cobalt-based high-temperature alloys, thereby obtaining cobalt-based high-temperature alloy welded joints with high tensile strength and high welding rate.

[0004] In order to achieve the above object, the present invention adopts the following technical solution:

[0005] On the one hand, the present invention provides an amorphous foil intermediate layer for TLP diffusion welding, comprising the following components in percentage by mass: Cr 17.3-18.7%, W 4.7-6.3%, B 2.8-4.3%, Ta 0.37-0.43%, Co 4.7-6.3%, La 0-0.1% and Ni balance.

[0006] Preferably, the amorphous foil intermediate layer for TLP diffusion welding comprises the following components in percentage by mass: Cr 18%, W 5%, B 3%, Ta 0.4%, Co 5%, La 0.05% and Ni balance.

[0007] In another aspect, the present invention further provides a use of the above-mentioned amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys.

[0008] Preferably, the application of the amorphous foil intermediate layer in the welding of cobalt-based high-temperature alloys comprises the following steps:

[0009] (1) placing at least one layer of the amorphous foil intermediate layer between a first plate and a second plate for positioning and fixing to obtain a component to be welded;

[0010] (2) The components to be welded are welded by TLP diffusion welding.

[0011] Preferably, the first plate material and / or the second plate material is a cobalt-based high-temperature alloy.

[0012] Preferably, the welding temperature of the TLP diffusion welding in step (2) is 1120-1180° C. and the holding time is 30-90 min.

[0013] Preferably, the TLP diffusion welding is performed in a vacuum furnace, and the heating process of the vacuum furnace is as follows:

[0014] Heat from room temperature to 300-440°C at a rate of 10-15°C / min and keep warm for 20 minutes;

[0015] Heat from 300-440℃ to 850-950℃ at a rate of 10-15℃ / min and keep warm for 40min;

[0016] Heat up from 850-950℃ to welding temperature at a rate of 10-15℃ / min, keep warm for 30-60min, and cool.

[0017] Preferably, before the positioning and fixing in step (1), the step further includes connecting the amorphous foil intermediate layer to the first plate material and / or the second plate material.

[0018] Preferably, the positioning and fixing and the connecting are both bonding or welding.

[0019] Preferably, the welding is micro-resistance spot welding, and the parameters of the micro-resistance spot welding are as follows: welding time 10-30 min, welding current 0.9-2.1 kA, welding pressure 80-120 N, pre-pressing time 800-1200 ms, and holding time 1500-2500 ms.

[0020] Preferably, the total thickness of the amorphous foil intermediate layer between the first plate and the second plate is 40-80 μm.

[0021] Preferably, when performing the TLP diffusion welding, a ceramic plate and a graphite pad are sequentially provided at the bottom of the component to be welded, and a graphite mold and a counterweight are sequentially provided at the top of the component to be welded.

[0022] Preferably, a groove matching the component to be welded is provided on one side of the graphite mold, so that the graphite mold is tightly pressed against the outer side of the component to be welded.

[0023] The present invention provides an amorphous foil intermediate layer for TLP diffusion welding and its application. Compared with the prior art, its beneficial effects are:

[0024] The amorphous foil intermediate layer for TLP diffusion welding with specific elements and proportions provided by the present invention is suitable for welding cobalt-based high-temperature alloys. The joint formed by welding the amorphous foil intermediate layer to the cobalt-based high-temperature alloy has excellent tensile strength and high welding rate. BRIEF DESCRIPTION OF THE DRAWINGS

[0025] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings required for use in the embodiments or the description of the prior art will be briefly introduced below. Obviously, the drawings described below are only embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on the provided drawings without paying creative work.

[0026] Figure 1 This is a schematic diagram of a product of an amorphous foil intermediate layer for TLP diffusion welding of the present invention;

[0027] Figure 2 This is a schematic diagram of temperature changes in a vacuum furnace in Example 1 of the present invention;

[0028] Figure 3 It is a schematic diagram of the structure during TLP diffusion welding.

[0029] In the figure: 1-graphite pad, 2-ceramic plate, 3-graphite mold, 4-weight block, 5-first plate, 6-amorphous foil middle layer, 7-second plate. DETAILED DESCRIPTION

[0030] The present invention will be described below by specific examples, and it will be appreciated by those skilled in the art that the following specific examples are only for illustrative purposes, and do not limit the scope of the present invention in any way. In addition, in the following examples, unless otherwise specified, the reagents and equipment used are all commercially available. If in the following examples, specific treatment conditions and treatment methods are not clearly described, then conditions and methods known in the art can be used to process.

[0031] In one aspect of the present invention, the present invention provides an amorphous foil intermediate layer for TLP diffusion welding, comprising the following components in percentage by mass: Cr 17.3-18.7%, W 4.7-6.3%, B 2.8-4.3%, Ta 0.37-0.43%, Co 4.7-6.3%, La 0-0.1% and Ni balance.

[0032] In some embodiments of the present invention, the amorphous foil intermediate layer for TLP diffusion welding includes the following components in percentage by mass: Cr 18%, W 5%, B 3%, Ta 0.4%, Co 5%, La 0.05% and the balance Ni.

[0033] In the present invention, based on high-temperature alloy elements, main alloy elements such as Ni, Cr, and W are retained, and interstitial element B that diffuses faster in the alloy is added as a melting-reducing element. By adding the B element, the melting point of the cobalt-based high-temperature alloy can be controlled so that a solid solution structure can be obtained more quickly in the connection area to improve the joint performance. According to the Inoue three empirical principles, the diversity of element types can change the amorphous degree of the middle layer. By adding La elements and rare earth elements Ta, the diversity of element types can be increased, and the amorphous degree of the middle layer can be changed, wherein Ta can increase the amorphous degree of the middle layer, reduce the liquidus temperature of the middle layer, and improve the high-temperature strength of the joint. The increase in La content can reduce the degree of dendrite segregation in the GH5188 alloy and change the precipitation morphology of the precipitated phase, and the alloy's long-lasting life can be significantly improved as the La content increases. The La element diffuses into the base material in the liquid phase, which is also beneficial to improving the base material performance. By adding a small amount of Co element, the liquidus line of the middle layer will be reduced and the high-temperature strength of the joint will be improved.

[0034] It should be noted that the parent material in the present invention refers to the first plate and the second plate; the amorphous foil intermediate layer for TLP diffusion welding is prepared by strip-spinning the intermediate layer alloy material, and the intermediate layer alloy material is prepared by vacuum melting technology.

[0035] In another aspect, the present invention further provides a use of the above-mentioned amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys.

[0036] In some embodiments of the present invention, the use of the amorphous foil intermediate layer in the welding of cobalt-based high-temperature alloys comprises the following steps:

[0037] (1) placing at least one layer of the amorphous foil intermediate layer between a first plate and a second plate for positioning and fixing to obtain a component to be welded;

[0038] (2) The components to be welded are welded by TLP diffusion welding.

[0039] In some embodiments of the present invention, before step (1), the first plate and the second plate to be welded are taken and pre-treated.

[0040] In this step, the first plate and the second plate are both metal alloys, and at least the first plate and the second plate are both cobalt-based high-temperature alloys, for example, GH5188 cobalt-based high-temperature alloy.

[0041] In some embodiments of the present invention, the pretreatment mainly includes surface defect detection, pre-welding cleaning and drying of the first plate and the second plate. Pre-welding cleaning includes grinding the surfaces of the first plate and the second plate until the scratches are consistent, and then wiping and cleaning with solvents such as acetone or alcohol to remove dirt such as oil, dirt, rust, burrs, etc. on the plates. The plates must not have defects such as cracks, processing damage, and flame cutting slag; drying is to clean the plates and let them stand for a period of time at room temperature to dry naturally. The standing time is generally >0.5h, and there is no special limitation on this, which can be adjusted according to actual conditions.

[0042] In some embodiments of the present invention, after the pretreatment, at least one layer of the amorphous foil intermediate layer is placed between the first plate and the second plate to be positioned and fixed, thereby obtaining a component to be welded.

[0043] In some embodiments of the present invention, before the positioning and fixing, the amorphous foil intermediate layer is also connected to the first plate and / or the second plate, the total thickness of the amorphous foil intermediate layer is 40-80μm, the thickness of the single-layer amorphous foil intermediate layer can be, for example, 15μm, 20μm, etc., the total thickness of the amorphous foil intermediate layer can be determined according to the thickness of the single-layer amorphous foil intermediate layer. The number of layers of the amorphous foil intermediate layer between the first plate and the second plate. For example, when the thickness of one layer of amorphous foil intermediate layer can reach the preset thickness, the layer of amorphous foil intermediate layer can be connected to any one of the first plate and the second plate for positioning and fixing, and when the thickness of two or more layers of amorphous foil intermediate layers can reach the preset thickness, multiple layers of amorphous foil intermediate layers can be connected to the first plate and the second plate, respectively, and this can be adjusted according to actual conditions.

[0044] In some embodiments of the present invention, the connection is bonding or welding, wherein bonding is bonding by adhesive, and welding is achieved by micro-resistance spot welding. The micro-resistance spot welding process can be performed by a micro-resistance spot welding machine, and the parameters of micro-resistance spot welding are as follows: welding time 10-30min, welding current 0.9-2.1kA, welding pressure 80-120N, pre-pressing time 800-1200ms, and holding time 1500-2500ms. Among them, the welding time can be, for example, 10min, 20min, 30min, etc., the welding current can be, for example, 0.9kA, 1.5kA, 2.1kA, etc., the welding pressure can be, for example, 80N, 100N, 120N, etc., the pre-pressing time can be, for example, 800ms, 1000ms, 1200ms, etc., and the holding time can be, for example, 1500ms, 2000ms, 2500ms, etc. The process parameters that have a significant impact on the performance of micro-resistance spot welding joints are mainly welding current, welding time and welding pressure. Specifically, changes in welding pressure will significantly change the contact resistance of the workpiece during micro-resistance spot welding. The welding current has the most significant impact on joint performance. Once the current is too large, it is easy to cause electrode sticking. Preferably, the middle layer of the amorphous foil is spot welded once every 10-30 mm, and the cross-sectional area of ​​the middle layer of the amorphous foil is slightly larger than the cross-sectional area of ​​the first plate and the second plate to make the welding more complete.

[0045] In some embodiments of the present invention, the positioning and fixing method can be bonding or welding, wherein the bonding is bonding by adhesive bonding, and the welding is micro-resistance spot welding, and the parameters of micro-resistance spot welding are the same as the parameters used in the above-mentioned connection process, which will not be repeated here. Preferably, the positioning and fixing method adopts the welding method of micro-resistance spot welding. This is because the area of ​​the sample is large, and if the welding surface is continuously coated with adhesive for bonding, the intense volatilization at high temperature may affect the vacuum degree of the vacuum furnace.

[0046] In some embodiments of the present invention, after obtaining the components to be welded, the components to be welded are welded by TLP diffusion welding to obtain a welded workpiece.

[0047] In this step, TLP diffusion welding is performed in a vacuum furnace, and the welding temperature of TLP diffusion welding is 1120-1180°C and the holding time is 30-90min. The welding temperature can be, for example, 1120°C, 1130°C, 1140°C, 1150°C, 1160°C, 1170°C, 1180°C, etc., and the holding time can be, for example, 30min, 40min, 50min, 60min, 70min, 80min, 90min, etc. The setting of welding temperature and holding time will affect the weld microstructure and mechanical properties of the joint. If the welding temperature is too low, carbide precipitation is likely to occur in the weld area, resulting in a decrease in the tensile strength of the joint; if the welding temperature is too high, exceeding the solution treatment temperature of the parent material, it is easy to damage the parent material performance; the length of the holding time can affect the diffusion process, and the extension of the holding time can increase the width of the isothermal solidification zone (ISZ) of the weld.

[0048] In some embodiments of the present invention, the heating process of the vacuum furnace is as follows: heating from room temperature to 300-440°C at a rate of 10-15°C / min, then keeping warm for 20 minutes, then heating from 300-440°C to 850-950°C at a rate of 10-15°C / min, then keeping warm for 40 minutes, and finally heating from 850-950°C to welding temperature at a rate of 10-15°C / min, then keeping warm for 60 minutes, and cooling. Preferably, cooling can be furnace cooling or cooling at a rate of 6°C / min, which is not particularly limited. The first heating process is used to remove the adhesive, and since the amount of adhesive used is small, there is no need for too long a holding time; the second heating process is used to further fit the intermediate layer material to the welded material under pressure.

[0049] In some embodiments of the present invention, when performing the TLP diffusion welding, the bottom of the assembly to be welded is provided with a ceramic plate 2 and a graphite pad 1 in sequence, and the top of the assembly to be welded is provided with a graphite mold 3 and a counterweight 4 in sequence, that is, the placement order from bottom to top is graphite pad 1, ceramic plate 2, assembly to be welded (second plate 7, amorphous foil strip middle layer 6, first plate 5), graphite mold 3 and counterweight 4; wherein the ceramic block 2 is used to prevent the amorphous foil strip middle layer 6 in the assembly to be welded from flowing out after high temperature liquid phase, and the counterweight 4 can be a metal block, and the weight can be, for example, 20kg, 25kg, etc. There is no special limitation on the weight of the counterweight 4, and it can compress the structure below the counterweight 4 to ensure the integrity and strength of the welding. Preferably, one side of the graphite mold 3 is provided with a groove adapted to the assembly to be welded, so that the graphite mold 3 is tightly compacted to the outside of the assembly to be welded.

[0050] In some embodiments of the present invention, after TLP diffusion welding, the process further includes cleaning and cutting the welded workpiece.

[0051] In this step, the cleaning is to take out the welded workpiece after the environment in the vacuum furnace drops to room temperature, wipe it with alcohol or clean it, and then air-dry it; the cutting is to use water cutting to cut off the required part of the welded workpiece, and then clean and air-dry the cut surface.

[0052] Example 1

[0053] This embodiment provides an amorphous foil intermediate layer for TLP diffusion welding, which is composed of the following components in percentage by mass: Ni 68.55%, Cr 18%, W 5%, B 3%, Ta0.4%, Co 5% and La 0.05%, and the thickness of the amorphous foil intermediate layer is 20 μm.

[0054] In this embodiment, the amorphous foil strip intermediate layer is used to weld the cobalt-based high-temperature alloy, and the specific steps are as follows:

[0055] (1) Take the first plate and the second plate to be welded as the base material for surface defect detection. After the surface defect detection is qualified, use 500-grit sandpaper to grind the surface until the scratches are consistent, then wipe with alcohol and air dry for 0.5h;

[0056] Wherein, the first plate and the second plate are both GH5188 cobalt-based high-temperature alloy.

[0057] (2) welding the middle layer of the two layers of amorphous foil to the first plate by micro-resistance spot welding, spot welding the middle layer of the amorphous foil once every 20 mm, and after the spot welding, the first plate and the second plate are positioned and fixed by an adhesive to obtain a component to be welded;

[0058] Among them, the cross-sectional area of ​​the middle layer of the amorphous foil is slightly larger than the cross-sectional area of ​​the first plate, the total thickness of the middle layer of the two layers of amorphous foil is 40μm, and the parameters of micro-resistance spot welding are as follows: welding time 20min, welding current 1.5kA, welding pressure 100N, pre-pressing time 1000ms, and holding time 2000ms.

[0059] (3) Using a vacuum furnace as a TLP diffusion welding container, a graphite pad, a ceramic plate, a component to be welded, a graphite mold, and a 20 kg counterweight are placed on the welding platform of the vacuum furnace from bottom to bottom, and the welding temperature is kept at 1150°C for 60 minutes to obtain a welded workpiece;

[0060] The heating process of the vacuum furnace is as follows: heating from room temperature to 300°C at a rate of 10°C / min and then keeping warm for 20 minutes, then heating from 300°C to 950°C at a rate of 10°C / min and then keeping warm for 40 minutes, and finally heating from 950°C to 1150°C at a rate of 10°C / min and then keeping warm for 60 minutes, and then cooling with the furnace.

[0061] (4) After the vacuum furnace environment drops to room temperature, take out the welded workpiece, wipe it with alcohol and air-dry it, use water cutting to cut the required part, clean it, air-dry it, and then test the tensile strength of the joint.

[0062] Example 2

[0063] Example 2 is basically the same as Example 1, with the only difference being that in step (2), the total thickness of the middle layer of the two amorphous foil strips is 60 μm.

[0064] Example 3

[0065] Example 3 is basically the same as Example 1, with the only difference being that in step (2), the total thickness of the middle layer of the two amorphous foil strips is 80 μm.

[0066] Example 4

[0067] Example 4 is basically the same as Example 1, with the only difference being that in step (3), the welding temperature is kept at 1120° C. for 60 minutes.

[0068] Example 5

[0069] Example 5 is basically the same as Example 1, with the only difference being that in step (3), the welding temperature is kept at 1180° C. for 60 minutes.

[0070] Example 6

[0071] Example 6 is basically the same as Example 1, with the only difference being that in step (3), the welding temperature is kept at 1150° C. for 30 minutes.

[0072] The room temperature tensile strength and 650°C high temperature tensile strength of the joints of Examples 1-6 were tested. The dimensions of the room temperature cylindrical tensile specimens (tensile specimen dimensions were formulated according to GB / T228.1-2010 standard) were as follows: total specimen length Lt = 78.66 mm, parallel length Lc = 30 mm, parallel portion diameter b = 5 mm, original gauge length L0 = 25 mm, clamping section length = 20 mm, diameter 10 mm, transition arc radius R = 5 mm. The parallel section roughness was Ra0.8, and the remaining section roughness was Ra1.6.

[0073] In particular, the high temperature tensile properties of Example 5 were tested, and the actual size of the high temperature tensile specimen was formulated according to GB / T228.2-2015 high temperature tensile specimen size.

[0074] The test results of each embodiment are shown in Table 1.

[0075] Table 1

[0076]

[0077] It can be seen from Table 1 that the microstructure and mechanical properties of GH5188 transient liquid phase diffusion welding (TLP) weld are affected by three factors: intermediate layer thickness, welding temperature and holding time.

[0078] Among them, the influence of the thickness of the intermediate layer on the microstructure and mechanical properties of the TLP weld: with the increase of the thickness of the intermediate layer, precipitation phases are generated in the center of the weld, and the types of precipitation phases mainly include Cr-rich MC and Cr-rich M2C; at the same time, with the increase of the thickness of the intermediate layer, the W element content in the weld decreases, and the density of the precipitation phase in the diffusion zone increases. When the thickness of the intermediate layer increases to 60 and 80 μm, the number of W-rich compounds increases sharply. The increase in W-rich compounds in the diffusion zone is the reason for the low W content in the weld; and with the increase of the thickness of the intermediate layer, the average tensile strength of the joint decreases.

[0079] Influence of welding temperature on the microstructure and mechanical properties of TLP welds: When the welding temperature is 1120℃, there is still a small amount of carbide in the center of the weld. As the temperature increases to 1150℃, the center of the weld is completely isothermally solidified. As the welding temperature increases, the width of the isothermal solidification zone and diffusion zone in the center of the weld increases, the density of the precipitated phase in the diffusion zone of the weld decreases, the needle-shaped precipitated phase gradually disappears, and the volume of the blocky precipitated phase is significantly reduced. When the welding temperature is 1180℃, the holding time is 60min, and the intermediate layer thickness is 40μm, the average tensile strength of the joint reaches 972MPa, accounting for about 92% of the parent material performance. There is a relatively obvious plastic deformation stage in the joint at 1180℃ / 60min, indicating that the tensile performance of the joint is excellent under this parameter. In addition, when the welding temperature is 1180℃, the holding time is 60min, the intermediate layer thickness is 40μm, the average tensile strength of the joint at 650℃ reaches 817MPa, which is close to the strength of the parent material in the same temperature range. There are a large number of dimples in the fracture of the joint. Tough fracture mainly occurs during high-temperature stretching, and the performance meets the use requirements.

[0080] Influence of holding time on microstructure and mechanical properties of TLP welds: Different holding times will affect the microstructure of the welds. With the increase of holding time, the width of the isothermal solidification zone and diffusion zone in the center of the weld increases. With the extension of holding time, there is no obvious difference in the diffusion zone (DAZ) of the weld.

[0081] Although the embodiments of the present invention have been shown and described above, it is to be understood that the above embodiments are exemplary and are not to be construed as limitations of the present invention. A person skilled in the art may change, modify, replace and vary the above embodiments within the scope of the present invention.

Claims

1. An amorphous foil intermediate layer for TLP diffusion bonding, characterized in that: The steel comprises the following components in percentage by mass: Cr 17.3-18.7%, W 4.7-6.3%, B 2.8-4.3%, Ta 0.37-0.43%, Co 4.7-6.3%, La 0-0.1% and Ni balance.

2. The amorphous foil intermediate layer for TLP diffusion bonding according to claim 1, characterized in that: The steel comprises the following components in percentage by mass: Cr 18%, W 5%, B 3%, Ta 0.4%, Co 5%, La 0.05% and the balance Ni.

3. Use of the amorphous foil intermediate layer according to any one of claims 1 to 2 in welding of cobalt-based high-temperature alloys.

4. The use of the amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys according to claim 3 is characterized in that: The following steps are involved: (1) placing at least one layer of the amorphous foil intermediate layer between a first plate and a second plate for positioning and fixing to obtain a component to be welded; (2) welding the components to be welded by TLP diffusion welding; The first plate and / or the second plate are / is made of a cobalt-based high-temperature alloy.

5. The use of the amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys according to claim 4, characterized in that: The welding temperature of the TLP diffusion welding in step (2) is 1120-1180° C. and the holding time is 30-90 min.

6. The use of the amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys according to claim 5, characterized in that: The TLP diffusion welding is performed in a vacuum furnace, and the heating process of the vacuum furnace is as follows: Heat from room temperature to 300-440°C at a rate of 10-15°C / min and keep warm for 20 minutes; Heat from 300-440℃ to 850-950℃ at a rate of 10-15℃ / min and keep warm for 40min; Heat up from 850-950℃ to welding temperature at a rate of 10-15℃ / min, keep warm for 30-90min, and cool.

7. The use of the amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys according to claim 4, characterized in that: Before the positioning and fixing in step (1), the method further includes connecting the amorphous foil intermediate layer to the first plate material and / or the second plate material.

8. The use of the amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys according to claim 7, characterized in that: The positioning and fixing and the connecting are both bonding or welding; The welding is micro-resistance spot welding, and the parameters of the micro-resistance spot welding are as follows: welding time 10-30min, welding current 0.9-2.1kA, welding pressure 80-120N, pre-pressing time 800-1200ms, and holding time 1500-2500ms.

9. The use of the amorphous foil intermediate layer in welding of cobalt-based high-temperature alloys according to claim 4, characterized in that: The total thickness of the amorphous foil intermediate layer between the first plate and the second plate is 40-80 μm.

10. Use of the amorphous foil intermediate layer according to any one of claims 4 to 9 in welding of cobalt-based high-temperature alloys, characterized in that: When performing the TLP diffusion welding, a ceramic plate and a graphite pad are sequentially arranged at the bottom of the assembly to be welded, and a graphite mold and a counterweight are sequentially arranged at the top of the assembly to be welded; A groove matched with the component to be welded is provided on one side of the graphite mold so that the graphite mold can be tightly pressed against the outer side of the component to be welded.

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