Nickel-based alloy welding wire and preparation method thereof

Abstract

The present disclosure relates to the field of welding technology, and provides a nickel-based alloy composite welding wire, comprising: a high-temperature nickel-based alloy welding wire, at least one nickel layer respectively located on at least one side of the high-temperature nickel-based alloy welding wire, and a niobium carbide layer located on the side of each nickel layer away from the high-temperature nickel-based alloy welding wire. The present disclosure also provides a method for preparing a nickel-based alloy composite welding wire, comprising: sequentially decontaminating, grinding and polishing the surface of the high-temperature nickel-based alloy welding wire to obtain a first welding wire; performing a first electrodeposition on at least one side of the first welding wire to form at least one nickel layer on at least one side of the first welding wire to obtain a second welding wire; performing a second electrodeposition on the side of each nickel layer of the second welding wire away from the high-temperature nickel-based alloy welding wire to form a niobium carbide layer. The present disclosure achieves the effect of effectively increasing the strain threshold for the initiation of high-temperature loss plastic cracking of high-temperature nickel-based alloys, and has a simple process and low cost.

Description

Technical Field

[0001] The present disclosure relates to the field of welding technology, for example, to a nickel-based alloy welding wire and a preparation method thereof. Background Art

[0002] Nuclear power high temperature nickel-based alloys (for example, Inconel690 alloy) have added strengthening elements such as Mo, Cr, Al, Nb, Mn, Si, etc., and have excellent corrosion resistance, wear resistance, high temperature tensile strength, high temperature fatigue strength, creep strength and oxidation resistance. They are the main structural materials for nuclear power pressure equipment. However, the alloy is prone to coarse columnar structure after welding, and high temperature loss cracks are prone to occur at 0.5-0.8TS, which seriously affects the service safety of the equipment. The direct cause of high temperature loss cracks is that the grain boundary strength of nuclear power high temperature nickel-based alloys in the above temperature range is lower than the intragranular strength, and because the grain boundary area is small and the stress concentration is large, intergranular cracking will occur under smaller stress.

[0003] At present, the main means to improve the high-temperature plastic crack sensitivity of nuclear power high-temperature nickel-based alloys is to add a certain amount of Nb, Mo and other elements to the brazing material, which can strengthen the solid solution atomic bonding force, slow down the softening rate, form MC carbides and Laves phases at the end of solidification, hinder the movement of the migration grain boundary during the cooling process, form curved grain boundaries, and thus increase the strain threshold for the high-temperature plastic crack of nuclear power high-temperature nickel-based alloys. However, the welding wire produced by this method is expensive, and the excessively high alloying element content in the welding wire will also lead to the segregation of the components at the end of solidification, thereby inducing crystallization cracks.

[0004] In summary, there is an urgent need for a method that can effectively increase the strain threshold for the initiation of high-temperature loss plastic cracking of high-temperature nickel-based alloys, and has a simple process and low cost. Summary of the invention

[0005] The purpose of the present invention is to overcome the shortcomings of the prior art and provide a nickel-based alloy composite welding wire and a preparation method thereof, so as to at least effectively increase the strain threshold for the initiation of high-temperature loss of plastic cracks in high-temperature nickel-based alloys, and to have a simple process and low cost.

[0006] The purpose of this disclosure is achieved through the following technical solutions:

[0007] In one aspect, a nickel-based alloy composite welding wire is provided, comprising a high-temperature nickel-based alloy welding wire, at least one nickel layer located on at least one side of the high-temperature nickel-based alloy welding wire, and a niobium carbide layer located on a side of each nickel layer away from the high-temperature nickel-based alloy welding wire.

[0008] It is easy to understand that at least one side of the high-temperature nickel-based alloy welding wire may be, for example, at least one side of the two sides in the extension direction of the high-temperature nickel-based alloy welding wire.

[0009] On this basis, the at least one nickel layer respectively located on at least one side of the high-temperature nickel-based alloy welding wire may, for example, be a nickel layer located on one side of the high-temperature nickel-based alloy welding wire (i.e., a nickel layer is provided on one of the two sides in the extension direction of the high-temperature nickel-based alloy welding wire), or may be two nickel layers respectively located on both sides of the high-temperature nickel-based alloy welding wire (i.e., a nickel layer is provided on both sides in the extension direction of the high-temperature nickel-based alloy welding wire).

[0010] It should be noted that the high-temperature nickel-based alloy welding wire disclosed herein may be, for example, a high-temperature nickel-based alloy welding wire based on a Ni-Cr-Fe matrix, and the disclosure does not limit the specific selection of the high-temperature nickel-based alloy welding wire based on the Ni-Cr-Fe matrix. For example, the high-temperature nickel-based alloy welding wire based on the Ni-Cr-Fe matrix may be welding wire FM52 or FM52M produced by Inconel Corporation of the United States, or may be a domestically produced high-temperature nickel-based alloy welding wire with similar material composition.

[0011] It is worth noting that in the nickel-based alloy composite welding wire provided in the embodiment of the present disclosure, the nickel layer and the niobium carbide layer located on the same side of the high-temperature nickel-based alloy welding wire are mechanically interlocked. On this basis, on the one hand, since the nickel layer has good ductility and the bonding interface between the nickel layer and the high-temperature nickel-based alloy welding wire (solid solution matrix) is good, therefore, by providing at least one nickel layer on at least one side of the high-temperature nickel-based alloy welding wire, respectively, the bonding force between the electrodeposited layer (i.e., the nickel layer and the niobium carbide layer) and the matrix (i.e., the high-temperature nickel-based alloy welding wire) can be enhanced; on the other hand, the Nb element is an important trace element of high-temperature nickel-based alloys, and Nb and C can combine to form niobium carbide, and niobium carbide can serve as the main strengthening phase of high-temperature nickel-based alloys, therefore, By providing the niobium carbide layer on the side of each nickel layer away from the high-temperature nickel-based alloy welding wire, the thermal crack resistance of the high-temperature nickel-based alloy can be improved and the mechanical strength of the material can be increased. In addition, since niobium carbide has a high melting point (higher than 3400°C), it can enter the molten pool in the form of a solid phase during welding. Therefore, the niobium carbide particles in the niobium carbide layer can also serve as nucleation cores for solidification of the molten pool, thereby refining the weld grains (formed after the molten pool crystallizes), pinning the grain boundaries to increase the tortuosity of the grain boundaries, etc., thereby significantly increasing the strain threshold for the initiation of high-temperature loss plastic cracks of the high-temperature nickel-based alloy.

[0012] It is worth noting that if there is an excessive amount of Nb element in the welding wire, it will cause obvious liquefaction cracking and solidification cracking sensitivity. The embodiment of the present disclosure avoids the occurrence of excessive Nb element being integrated into the weld matrix by directly providing the niobium carbide layer (i.e., niobium carbide solid phase particles) on the side of each nickel layer away from the high-temperature nickel-based alloy welding wire.

[0013] In some embodiments, in the nickel-based alloy composite welding wire, the volume fraction of all the niobium carbide layers is 0.3% to 0.8%.

[0014] In the above embodiment, by limiting the volume fraction of all the niobium carbide layers, not only the coating effect of the niobium carbide layers can be ensured, but also the probability of mutual collision and agglomeration of niobium carbide particles in the niobium carbide layers can be reduced, thereby ensuring uniform distribution of niobium carbide particles.

[0015] In some embodiments, the nickel layer has a thickness of 4-10 μm.

[0016] In the above embodiment, by limiting the thickness of the nickel layer, not only the uniformity of the deposition of the niobium carbide layer can be improved, but also the bonding strength of the niobium carbide layer, the nickel layer and the high-temperature nickel-based alloy welding wire can be improved. In addition, by limiting the thickness of the nickel layer, the buffering interface stress of the nickel layer can also be ensured.

[0017] In some embodiments, the niobium carbide layer has a thickness of 70-100 μm.

[0018] In the above embodiment, by limiting the thickness of the niobium carbide layer, not only can sufficient niobium carbide particles be introduced to ensure the improvement effect on the weld structure, but also the plasticity of the weld material can be ensured. In addition, by limiting the thickness of the niobium carbide layer, the deposition time can also be controlled to ensure the deposition efficiency.

[0019] On the other hand, a method for preparing a nickel-based alloy composite welding wire is provided. The preparation method comprises: sequentially performing decontamination, grinding and polishing treatments on the surface of a high-temperature nickel-based alloy welding wire to obtain a first welding wire; performing a first electrodeposition on at least one side surface of the first welding wire to form at least one nickel layer on at least one side surface of the first welding wire to obtain a second welding wire; performing a second electrodeposition on a side surface of each nickel layer of the second welding wire away from the high-temperature nickel-based alloy welding wire to form a niobium carbide layer on a side surface of each nickel layer of the second welding wire away from the high-temperature nickel-based alloy welding wire to obtain the nickel-based alloy composite welding wire.

[0020] In the method for preparing the nickel-based alloy composite welding wire provided in the embodiment of the present disclosure, on the one hand, by performing the first electrodeposition on at least one side of the high-temperature nickel-based alloy welding wire to form at least one nickel layer, the bonding force between the electrodeposited layer (i.e., the nickel layer and the niobium carbide layer) and the substrate (i.e., the high-temperature nickel-based alloy welding wire) can be enhanced; on the other hand, by performing the second electrodeposition on the side of each nickel layer away from the high-temperature nickel-based alloy welding wire to form the niobium carbide layer, not only the thermal crack resistance of the high-temperature nickel-based alloy can be improved and the mechanical strength of the material can be improved, but also the weld grains can be refined, the grain boundaries can be pinned to increase the grain boundary tortuosity, etc., thereby significantly improving the strain threshold for the high-temperature loss plastic crack of the high-temperature nickel-based alloy to start cracking. At the same time, the method for preparing the nickel-based alloy composite welding wire provided in the embodiment of the present disclosure also has the advantages of simple preparation process and low cost.

[0021] In addition, by sequentially decontaminating, grinding and polishing the surface of the high-temperature nickel-based alloy welding wire, not only can the bonding between the electrodeposited layer (i.e., the nickel layer and the niobium carbide layer) and the substrate be enhanced, but also the possibility of defects in the subsequent welding process can be reduced.

[0022] In some embodiments, the first electrodeposition is direct current electrodeposition.

[0023] In some embodiments, the electroplating solution used in the direct current electroplating is a Watt's solution, and the solute of the Watt's solution includes nickel sulfate hexahydrate, nickel chloride hexahydrate and boric acid.

[0024] It should be noted that the specific amount of each component included in the solute of the above-mentioned Watt solution can be selected and set according to needs, and the embodiments of the present disclosure are not limited to this.

[0025] In some examples, the mass volume ratio of the nickel sulfate hexahydrate is 150-400 g / L, the mass volume ratio of the nickel chloride hexahydrate is 10-40 g / L, and the mass volume ratio of the boric acid is 20-50 g / L.

[0026] In some embodiments, the process conditions of the direct current electrodeposition include: a current density of 1.0 to 3.5 A / dm 2 The electrodeposition time is 10 to 60 minutes, the electrodeposition temperature is 40 to 55°C, and the stirring speed is 200 to 400 r / min.

[0027] In some embodiments, the second electrodeposition is direct current electrodeposition.

[0028] In some embodiments, the solute of the electrodeposition solution used in the direct current electrodeposition includes niobium carbide particles, nickel sulfate hexahydrate, nickel chloride hexahydrate, boric acid and hexadecyltrimethylammonium bromide.

[0029] In the above embodiment, by selecting the cetyltrimethylammonium bromide (CTAB) as the cationic surfactant, the grain size of the niobium carbide layer can be significantly refined, thereby improving the hardness and tensile stress of the niobium carbide layer.

[0030] In some embodiments, the particle size of the niobium carbide particles is 3-8 μm.

[0031] In some examples, the niobium carbide particles are irregularly spherical in shape, have a purity greater than 99%, and need to be cleaned and dried before use to remove impurities and moisture.

[0032] In the above example, niobium carbide particles with a particle size of 3 to 8 μm and an irregular spherical shape are selected as ceramic additive particles. In this case, the density of the niobium carbide particles is 7.79 g / cm 3 , which is closer to the density of the high-temperature nickel-based alloy, thereby reducing the impact of uneven distribution of ceramic additive particles in the electrodeposited layer (ie, the niobium carbide layer); at the same time, the niobium carbide particles have good thermodynamic stability and are not easy to decompose at high temperatures.

[0033] It should be noted that the specific amount of each component included in the solute of the above-mentioned electrodeposition solution can be selected and set according to needs, and the embodiments of the present disclosure are not limited to this.

[0034] In some examples, the mass volume ratio of the niobium carbide particles is 20-50 g / L, the mass volume ratio of the nickel sulfate hexahydrate is 150-400 g / L, the mass volume ratio of the nickel chloride hexahydrate is 10-40 g / L, the mass volume ratio of the boric acid is 20-50 g / L, and the mass volume ratio of the hexadecyltrimethylammonium bromide is 0.1-0.5 g / L.

[0035] In some embodiments, the process conditions of the second electrodeposition include: a current density of 2 to 4 A / dm 2 , the electrodeposition time is 0.5 to 2 h, the electrodeposition temperature is 40 to 55 ° C, and the stirring speed is 200 to 400 r / min.

[0036] It should be noted that the volume fraction and thickness of the niobium carbide layer (i.e., the content of niobium carbide particles) can be adjusted by controlling the electrodeposition time. Specifically, the longer the electrodeposition time, the higher the content of niobium carbide particles; the shorter the electrodeposition time, the lower the content of niobium carbide particles.

[0037] In some embodiments, the decontamination is performed by at least one of vapor degreasing and acetone cleaning.

[0038] In some embodiments, the grinding refers to grinding using at least one of a grinder and sandpaper.

[0039] In some embodiments, before performing the first electrodeposition, the method further includes performing a first ultrasonic cleaning on the first welding wire.

[0040] In some examples, the cleaning liquid used in the first ultrasonic cleaning is alcohol, and the time of the first ultrasonic cleaning is 5 to 20 minutes.

[0041] In some embodiments, before performing the second electrodeposition, the method further includes performing a second ultrasonic cleaning on the second welding wire.

[0042] In some examples, the cleaning liquid used in the second ultrasonic cleaning is alcohol, and the time of the second ultrasonic cleaning is 5 to 20 minutes.

[0043] The nickel-based alloy welding wire and the preparation method thereof provided by the present disclosure have the following beneficial effects:

[0044] 1. A nickel-based alloy welding wire disclosed in the present invention can enhance the bonding force between the electrodeposited layer and the substrate by providing at least one nickel layer on at least one side of the high-temperature nickel-based alloy welding wire.

[0045] 2. A nickel-based alloy welding wire disclosed in the present invention, by providing the niobium carbide layer on the side of each nickel layer away from the high-temperature nickel-based alloy welding wire, can not only improve the thermal crack resistance of the high-temperature nickel-based alloy and enhance the mechanical strength of the material, but also can refine the weld grains, pin the grain boundaries to increase the grain boundary tortuosity, etc., thereby significantly increasing the strain threshold for the initiation of high-temperature loss plastic cracking of the high-temperature nickel-based alloy.

[0046] 3. The method for preparing a nickel-based alloy welding wire disclosed in the present invention also has the advantages of simple preparation process and low cost. BRIEF DESCRIPTION OF THE DRAWINGS

[0047] In order to more clearly illustrate the technical solutions in the present disclosure, the following briefly introduces the drawings required for use in some embodiments of the present disclosure. Obviously, the drawings described below are only drawings of some embodiments of the present disclosure. For those of ordinary skill in the art, other drawings can also be obtained based on these drawings. In addition, the drawings described below can be regarded as schematic diagrams, and are not limitations on the actual size of the products involved in the embodiments of the present disclosure and the actual process of the method.

[0048] Figure 1 is a schematic diagram of a nickel-based alloy composite welding wire according to the present disclosure;

[0049] Figure 2is a flow chart of a method for preparing a nickel-based alloy composite welding wire according to the present disclosure;

[0050] Figure 3 This is a weld grain morphology diagram of the nickel-based alloy composite welding wire in Example 1 after TIG surfacing;

[0051] Figure 4 This is a grain morphology diagram of the weld of the nickel-based alloy composite welding wire in comparative example 1 after TIG surfacing;

[0052] Figure 5 This is a weld grain morphology diagram of the nickel-based alloy composite welding wire in Example 2 after TIG surfacing;

[0053] Figure 6 This is the weld grain morphology of the nickel-based alloy composite welding wire in Control Example 2 after TIG surfacing. DETAILED DESCRIPTION

[0054] The technical solutions in some embodiments of the present disclosure are described clearly and completely below. Obviously, the described embodiments are only part of the embodiments of the present disclosure, not all of the embodiments. Based on the embodiments provided by the present disclosure, all other embodiments obtained by ordinary technicians in this field belong to the scope of protection of the present disclosure.

[0055] Unless the context requires otherwise, throughout the specification and claims, the term "including" is to be interpreted as an open, inclusive meaning, that is, "including, but not limited to". In the description of the specification, the terms "one embodiment", "some embodiments", "exemplary embodiments", "example", "specific example" or "some examples" and the like are intended to indicate that specific features, structures, materials or characteristics associated with the embodiment or example are included in at least one embodiment or example of the present disclosure. The schematic representation of the above terms does not necessarily refer to the same embodiment or example. In addition, the specific features, structures, materials or characteristics may be included in any one or more embodiments or examples in any appropriate manner.

[0056] In the following, the terms "first" and "second" are used for descriptive purposes only and are not to be understood as indicating or implying relative importance or implicitly indicating the number of the indicated technical features. Thus, a feature defined as "first" or "second" may explicitly or implicitly include one or more of the features. In the description of the embodiments of the present disclosure, unless otherwise specified, "plurality" means two or more.

[0057] When describing some embodiments, the expression "A and / or B" may be used. It is easy to understand that "A and / or B" includes the following three combinations: only A, only B, and a combination of A and B.

[0058] Example 1

[0059] 1. A nickel-based alloy composite welding wire 1, such as Figure 1 As shown, it includes: a high-temperature nickel-based alloy welding wire 11, two nickel layers 12 respectively located on both sides of the extension direction of the high-temperature nickel-based alloy welding wire 11, and a niobium carbide layer 13 located on the side of each nickel layer 12 away from the high-temperature nickel-based alloy welding wire 11.

[0060] In the nickel-based alloy composite welding wire 1, the volume fraction of all niobium carbide layers 13 is 0.4%; the thickness of each nickel layer 12 is 7 μm, and the thickness of each niobium carbide layer 13 is 100 μm.

[0061] 2. A method for preparing the nickel-based alloy composite welding wire 1, as Figure 2 The preparation method specifically comprises: S1 to S3.

[0062] S1. The surface of the high-temperature nickel-based alloy welding wire 11 is steam degreased and cleaned with acetone to remove contaminants from the surface, and then the decontaminated surface is polished to a bright finish using a grinder and sandpaper, and finally the polished surface is polished to obtain a first welding wire.

[0063] S2. Use alcohol to ultrasonically clean the first welding wire for 15 minutes, and perform direct current electrodeposition on the two side surfaces of the first welding wire in the extension direction after ultrasonic cleaning, so as to form two nickel layers 12 on the two side surfaces in the extension direction of the first welding wire respectively (that is, a nickel layer 12 is formed on each of the two side surfaces in the extension direction of the first welding wire), to obtain a second welding wire.

[0064] The electroplating solution used in the DC electroplating is a Watt solution, and the solutes of the Watt solution include 250 g / L nickel sulfate hexahydrate, 20 g / L nickel chloride hexahydrate and 35 g / L boric acid in terms of mass volume ratio. The process conditions of the DC electroplating include: a current density of 2 A / dm 2 , the electrodeposition time is 15 min, the electrodeposition temperature is 45 °C, and the stirring speed is 300 r / min.

[0065] S3. Use alcohol to ultrasonically clean the second welding wire for 15 minutes, and perform direct current electrodeposition on the surface of the side of each nickel layer 12 of the second welding wire away from the high-temperature nickel-based alloy welding wire 11 after ultrasonic cleaning, so as to form a niobium carbide layer 13 on the surface of the side of each nickel layer 12 of the second welding wire away from the high-temperature nickel-based alloy welding wire 11.

[0066] Wherein, the solutes of the electroplating solution used in the above-mentioned direct current electroplating include 20g / L niobium carbide particles, 250g / L nickel sulfate hexahydrate, 20g / L nickel chloride hexahydrate, 35g / L boric acid and 0.4g / L hexadecyltrimethylammonium bromide, calculated by mass volume ratio; wherein, the average particle size of the above-mentioned niobium carbide particles is 3μm, the shape is irregular spherical, the purity is greater than 99%, and it needs to be cleaned and dried before use to remove impurities and moisture. The process conditions of the above-mentioned direct current electroplating include: the current density is 4A / dm 2 , the electrodeposition time is 2h, the electrodeposition temperature is 45℃, and the stirring speed is 300r / min.

[0067] It should be noted that the high-temperature nickel-based alloy welding wire 11 in this embodiment is the welding wire FM52M produced by Inconel Corporation of the United States.

[0068] Comparative Example 1

[0069] For the nickel-based alloy composite welding wire provided in this comparative example, its preparation method has the same steps and conditions as the preparation method in Example 1 of the present disclosure, except that S3 is not included.

[0070] Experimental results

[0071] In order to verify the performance of the nickel-based alloy composite welding wire disclosed in the present invention, TIG surfacing (Tungsten Inert Gas Welding) was performed on the nickel-based alloy composite welding wires of Example 1 and Comparative Example 1, respectively, and the process conditions are shown in the following table:

[0072]

[0073] Depend on Figures 3-4 It can be seen that compared with Control Example 1, the nickel-based alloy composite welding wire of Example 1 adds niobium carbide particles with a volume fraction of 0.4% and an average particle size of 3 μm, the weld grains are refined and the grain boundaries are more tortuous; in addition, the average grain size of the nickel-based alloy composite welding wire of Example 1 is 71.5 μm, while the average grain size of the nickel-based alloy composite welding wire of Control Example 1 is 105 μm.

[0074] Example 2

[0075] 1. A nickel-based alloy composite welding wire 1, such as Figure 1 As shown, it includes: a high-temperature nickel-based alloy welding wire 11, two nickel layers 12 respectively located on both sides of the extension direction of the high-temperature nickel-based alloy welding wire 11, and a niobium carbide layer 13 located on the side of each nickel layer 12 away from the high-temperature nickel-based alloy welding wire 11.

[0076] In the nickel-based alloy composite welding wire 1, the volume fraction of all niobium carbide layers 13 is 0.8%; the thickness of each nickel layer 12 is 7 μm, and the thickness of each niobium carbide layer 13 is 100 μm.

[0077] 2. A method for preparing the nickel-based alloy composite welding wire 1, as Figure 2 The preparation method specifically comprises: S1 to S3.

[0078] S1. The surface of the high-temperature nickel-based alloy welding wire 11 is steam degreased and cleaned with acetone to remove contaminants from the surface, and then the decontaminated surface is polished to a bright finish using a grinder and sandpaper, and finally the polished surface is polished to obtain a first welding wire.

[0079] S2. Use alcohol to ultrasonically clean the first welding wire for 15 minutes, and perform direct current electrodeposition on the two side surfaces of the first welding wire in the extension direction after ultrasonic cleaning, so as to form two nickel layers 12 on the two side surfaces in the extension direction of the first welding wire respectively (that is, a nickel layer 12 is formed on each of the two side surfaces in the extension direction of the first welding wire), to obtain a second welding wire.

[0080] The electroplating solution used in the DC electroplating is a Watt solution, and the solutes of the Watt solution include 250 g / L nickel sulfate hexahydrate, 20 g / L nickel chloride hexahydrate and 35 g / L boric acid in terms of mass volume ratio. The process conditions of the DC electroplating include: a current density of 2 A / dm 2 , the electrodeposition time is 15 min, the electrodeposition temperature is 45 °C, and the stirring speed is 300 r / min.

[0081] S3. Use alcohol to ultrasonically clean the second welding wire for 15 minutes, and perform direct current electrodeposition on the surface of the side of each nickel layer 12 of the second welding wire away from the high-temperature nickel-based alloy welding wire 11 after ultrasonic cleaning, so as to form a niobium carbide layer 13 on the surface of the side of each nickel layer 12 of the second welding wire away from the high-temperature nickel-based alloy welding wire 11.

[0082] Among them, the solutes of the electroplating solution used in the above-mentioned direct current electroplating include 33g / L niobium carbide particles, 250g / L nickel sulfate hexahydrate, 20g / L nickel chloride hexahydrate, 35g / L boric acid and 0.4g / L hexadecyltrimethylammonium bromide, calculated by mass volume ratio; wherein the average particle size of the above-mentioned niobium carbide particles is 3μm, the shape is irregular spherical, the purity is greater than 99%, and it needs to be cleaned and dried before use to remove impurities and moisture. The process conditions of the above-mentioned direct current electroplating include: the current density is 4A / dm 2 , the electrodeposition time is 2h, the electrodeposition temperature is 45℃, and the stirring speed is 300r / min.

[0083] It should be noted that the high-temperature nickel-based alloy welding wire 11 in this embodiment is the welding wire FM52M produced by Inconel Corporation of the United States.

[0084] Comparative Example 2

[0085] For the nickel-based alloy composite welding wire provided in this comparative example, its preparation method has the same steps and conditions as the preparation method in Example 2 of the present disclosure, except that S3 is not included.

[0086] Experimental results

[0087] In order to verify the performance of the nickel-based alloy composite welding wire disclosed in the present invention, TIG surfacing (Tungsten Inert Gas Welding) was performed on the nickel-based alloy composite welding wires of Example 2 and Comparative Example 2, respectively, and the process conditions are shown in the following table:

[0088]

[0089] Depend on Figures 5-6 It can be seen that compared with Control Example 2, the nickel-based alloy composite welding wire of Example 2 adds niobium carbide particles with a volume fraction of 0.8% and an average particle size of 3 μm, and the weld grain refinement and grain boundary tortuosity effects are more obvious; in addition, the average grain size of the nickel-based alloy composite welding wire of Example 2 is 37.5 μm, while the average grain size of the nickel-based alloy composite welding wire of Control Example 2 is 105 μm.

[0090] Based on the above-mentioned Examples 1 to 2 and Comparative Examples 1 to 2, it can be known that introducing a small amount of uniformly dispersed niobium carbide particles into the high-temperature nickel-based alloy welding wire can play a role in refining the grains, pinning the grain boundaries to increase the tortuosity of the grain boundaries, etc., which can significantly increase the strain threshold for the initiation of high-temperature loss plastic cracking of the high-temperature nickel-based alloy.

[0091] In summary, the nickel-based alloy composite welding wire and the preparation method thereof disclosed in the present invention effectively improve the strain threshold for the initiation of high-temperature loss plastic cracking of high-temperature nickel-based alloys, and have the effects of simple process and low cost.

[0092] The above is only a preferred embodiment of the present disclosure. It should be understood that the present disclosure is not limited to the form disclosed herein, and should not be regarded as excluding other embodiments, but can be used in various other combinations, modifications and environments, and can be modified within the scope of the concept described herein through the above teachings or the technology or knowledge of the relevant field. The changes and modifications made by those skilled in the art do not deviate from the spirit and scope of the present disclosure, and should be within the scope of protection of the claims attached to the present disclosure.

Claims

1. A nickel-based alloy composite welding wire, characterized in that: include: High temperature nickel-based alloy welding wire; at least one nickel layer respectively located on at least one side of the high temperature nickel-based alloy welding wire; as well as a niobium carbide layer located on a side of each nickel layer away from the high temperature nickel-based alloy welding wire; In the nickel-based alloy composite welding wire, the volume fraction of all the niobium carbide layers is 0.3% to 0.8%.

2. The nickel-based alloy composite welding wire according to claim 1, characterized in that: The thickness of the nickel layer is 4-10 μm; And / or, the thickness of the niobium carbide layer is 70-100 μm.

3. A method for preparing a nickel-based alloy composite welding wire, characterized in that: include: Decontamination, grinding and polishing are sequentially performed on the surface of the high-temperature nickel-based alloy welding wire to obtain a first welding wire; Performing a first electrodeposition on at least one side surface of the first welding wire to form at least one nickel layer on at least one side surface of the first welding wire to obtain a second welding wire; A second electrodeposition is performed on the surface of one side of each nickel layer of the second welding wire away from the high-temperature nickel-based alloy welding wire to form a niobium carbide layer on the surface of one side of each nickel layer of the second welding wire away from the high-temperature nickel-based alloy welding wire to obtain the nickel-based alloy composite welding wire; wherein, in the nickel-based alloy composite welding wire, the volume fraction of all the niobium carbide layers is 0.3%~0.8%.

4. The preparation method according to claim 3, characterized in that: The first electrodeposition is direct current electrodeposition.

5. The preparation method according to claim 4, characterized in that: The electroplating solution used in the direct current electroplating is a Watt solution, and the solute of the Watt solution includes nickel sulfate hexahydrate, nickel chloride hexahydrate and boric acid; And / or, the process conditions of the direct current electrodeposition include: a current density of 1.0 to 3.5 A / dm 2 , the electrodeposition time is 10~60min, the electrodeposition temperature is 40~55℃, and the stirring speed is 200~400r / min.

6. The preparation method according to claim 3, characterized in that: The second electrodeposition is direct current electrodeposition.

7. The preparation method according to claim 6, characterized in that: The solute of the electrodeposition solution used in the direct current electrodeposition includes niobium carbide particles, nickel sulfate hexahydrate, nickel chloride hexahydrate, boric acid and hexadecyltrimethylammonium bromide; And / or, the process conditions of the second electrodeposition include: a current density of 2-4 A / dm 2 , the electrodeposition time is 0.5~2h, the electrodeposition temperature is 40~55℃, and the stirring speed is 200~400r / min.

8. The preparation method according to claim 7, characterized in that: The particle size of the niobium carbide particles is 3-8 μm.

9. The preparation method according to claim 3, characterized in that: Decontamination refers to decontamination by at least one of steam degreasing and acetone cleaning; And / or, the grinding refers to grinding using at least one of a grinder and sandpaper; And / or, before performing the first electrodeposition, the step of performing a first ultrasonic cleaning on the first welding wire is also included; And / or, before performing the second electrodeposition, the method further includes performing a second ultrasonic cleaning on the second welding wire.

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