CN117259885A - Method for brazing zirconium alloy and high-entropy alloy by adopting laser cladding Nb - Google Patents
Method for brazing zirconium alloy and high-entropy alloy by adopting laser cladding Nb Download PDFInfo
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- CN117259885A CN117259885A CN202311430220.3A CN202311430220A CN117259885A CN 117259885 A CN117259885 A CN 117259885A CN 202311430220 A CN202311430220 A CN 202311430220A CN 117259885 A CN117259885 A CN 117259885A
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 61
- 239000000956 alloy Substances 0.000 title claims abstract description 61
- 238000005219 brazing Methods 0.000 title claims abstract description 53
- 229910001093 Zr alloy Inorganic materials 0.000 title claims abstract description 43
- 238000000034 method Methods 0.000 title claims abstract description 22
- 238000004372 laser cladding Methods 0.000 title claims abstract description 21
- 238000005253 cladding Methods 0.000 claims abstract description 44
- 239000011888 foil Substances 0.000 claims abstract description 17
- 229910052751 metal Inorganic materials 0.000 claims abstract description 15
- 239000002184 metal Substances 0.000 claims abstract description 15
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 239000000945 filler Substances 0.000 claims abstract description 11
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 238000003466 welding Methods 0.000 claims abstract description 11
- 238000005498 polishing Methods 0.000 claims abstract description 7
- 238000004140 cleaning Methods 0.000 claims abstract description 3
- 244000137852 Petrea volubilis Species 0.000 claims description 23
- 239000000843 powder Substances 0.000 claims description 13
- 229910000679 solder Inorganic materials 0.000 claims description 13
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 12
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 6
- 239000006023 eutectic alloy Substances 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 3
- 238000006243 chemical reaction Methods 0.000 abstract description 9
- 230000005496 eutectics Effects 0.000 abstract description 8
- 239000000463 material Substances 0.000 abstract description 7
- 239000010953 base metal Substances 0.000 abstract description 5
- 230000007704 transition Effects 0.000 abstract description 3
- 238000010008 shearing Methods 0.000 abstract description 2
- 238000011065 in-situ storage Methods 0.000 abstract 1
- 238000007781 pre-processing Methods 0.000 abstract 1
- 229910052804 chromium Inorganic materials 0.000 description 13
- 229910052726 zirconium Inorganic materials 0.000 description 10
- 239000000243 solution Substances 0.000 description 6
- 239000012071 phase Substances 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 4
- 238000001035 drying Methods 0.000 description 4
- 238000004506 ultrasonic cleaning Methods 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000000446 fuel Substances 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 230000001105 regulatory effect Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000000306 component Substances 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 1
- 239000008358 core component Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000003758 nuclear fuel Substances 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 229910000601 superalloy Inorganic materials 0.000 description 1
Classifications
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/008—Soldering within a furnace
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/19—Soldering, e.g. brazing, or unsoldering taking account of the properties of the materials to be soldered
-
- 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
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/20—Preliminary treatment of work or areas to be soldered, e.g. in respect of a galvanic coating
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Laser Beam Processing (AREA)
Abstract
The invention relates to the technical field of zirconium alloy and high-entropy alloy welding, in particular to a method for braze welding high-entropy alloy and zirconium alloy by adopting laser cladding Nb, which comprises the steps of preparing an NbCoCrFeMnNi eutectic high-entropy alloy transition layer by in-situ reaction through laser cladding Nb on the surface of the high-entropy alloy, polishing and preprocessing the surface of a cladding layer and the surface of the zirconium alloy to obtain a base metal to be welded, cleaning the base metal to be welded and a Zr63.2Cu36.8wt.% brazing filler metal foil, placing the brazing filler metal foil between the two base metals to be welded to form a sample to be welded, placing the sample to be welded in a vacuum brazing furnace, and heating the sample to 1010 in a vacuum environment o C, keeping the brazing temperature at the brazing temperature for 10min, and then cooling to room temperature to obtain a brazed joint, wherein compared with the joint shearing performance of direct brazing by AgCu brazing filler metal, the joint obtained by auxiliary brazing through Nb laser claddingThe strength of the head is improved by 382%, and the high-quality connection of the zirconium alloy and the high-entropy alloy dissimilar materials is realized.
Description
Technical Field
The invention relates to the technical field of welding of zirconium alloy and high-entropy alloy, in particular to a method for braze welding of high-entropy alloy and zirconium alloy by adopting laser cladding Nb.
Background
The zirconium alloy has the characteristics of moderate mechanical property, smaller neutron absorption section, excellent processing capability, irradiation resistance, corrosion resistance, good compatibility with nuclear fuel and the like, and is widely used as an internal core component material of a nuclear reactor, such as a fuel cladding, a spacing grid and the like.
The high-entropy alloy (HEAs) is a chemically disordered solid solution alloy introduced by mixing 5-13 components, has excellent mechanical properties at low temperature and high temperature, and has good wear resistance and corrosion resistance, so that the alloy becomes one of potential structural materials in aerospace and nuclear industries. In particular, the cocrfennni HEA of Face Centered Cubic (FCC) structure has higher structural stability under He ion irradiation environment due to low mobility and point defects of He atoms thereof, compared to the commonly used end plug materials (stainless steel and nickel-based superalloy).
In a nuclear reactor, end plugs are usually welded to fuel cladding at two sides, and if the welding of CoCrFeMnNi high-entropy alloy and zirconium alloy fuel cladding which can be used as plug materials is realized, the manufacturing and application of high-entropy alloy structural materials in the nuclear field are facilitated, and the nuclear reactor with long service life and high reliability is of great significance. However, the CoCrFeMnNi high-entropy alloy has five components, so that the CoCrFeMnNi high-entropy alloy is easy to react with zirconium with high activity in the welding process to form a large number of zirconium-based brittle compounds, and the performance of the joint is affected; in addition, zirconium alloy (5.3X10) -6 K -1 ) With CoCrFeMnNi high entropy alloy (15×10) -6 K -1 ) There is a large difference in thermal expansion coefficient, and a large thermal residual stress is easily caused in the cooling process, deteriorating the joint performance.
Disclosure of Invention
Therefore, the application provides a method for braze welding of high-entropy alloy and zirconium alloy by adopting laser cladding Nb to solve the technical problems of large residual stress, large brittleness of welding lines and distribution of hardening compounds in the traditional welding process.
A method for brazing high-entropy alloy and zirconium alloy by adopting laser cladding to assist Nb comprises the following steps:
polishing the surface of the high-entropy alloy, and preparing a cladding layer on the surface of the high-entropy alloy by cladding Nb powder with laser;
polishing and pre-treating a surface to be welded of the zirconium alloy and a surface to be welded of a cladding layer formed by the high-entropy alloy, so as to obtain a parent metal to be welded, wherein a Zr63.2Cu36.8 (wt.%) eutectic alloy foil is used as a brazing filler metal;
step three, cleaning the zirconium alloy, the high-entropy alloy and the solder foil obtained in the step three by using acetone and absolute ethyl alcohol;
fourthly, placing the Zr63.2Cu36.8 brazing foil between the surfaces to be welded of the high-entropy alloy and the zirconium alloy to form a sample to be welded, placing the sample in a vacuum brazing furnace, heating the sample to a brazing temperature of 1010 ℃ in a vacuum environment, preserving heat for 10min at the brazing temperature, and cooling to room temperature; the high-entropy alloy is CoCrFeMnNi high-entropy alloy.
In the first step and the second step, the surfaces to be welded of the high-entropy alloy (before and after cladding) and the zirconium alloy are polished by using 180# metallographic sand paper, 400# metallographic sand paper, 800# metallographic sand paper, 1200# metallographic sand paper, 2000# metallographic sand paper and 3000# metallographic sand paper.
In the first step of the invention, the thickness of a cladding layer formed on the surface of the high-entropy alloy by cladding Nb powder by laser is 150-420 mu m.
In the first step of the invention, the Nb powder particle diameter is 45-105 mu m, and the parameters of laser cladding are power 800-1000W, scanning speed 1000mm/min and powder feeding speed 0.2-0.35r/min.
In the second step of the invention, the thickness of the Zr63.2Cu36.8 solder foil is 200 mu m.
In the third step of the invention, the zirconium alloy, the high-entropy alloy and the Zr63.2Cu36.8 solder foil are firstly ultrasonically cleaned for 30min by using acetone, then ultrasonically cleaned for 15min by using absolute ethyl alcohol, and dried.
The vacuum heating in the fourth step of the invention comprises the steps of -3 Heating under the vacuum condition of Pa or below, heating to brazing temperature at the speed of 10 ℃/min, preserving heat, cooling to 200 ℃ at the speed of 5 ℃/min after brazing, and finally cooling to room temperature along with a furnace.
Compared with the prior art, the invention has the advantages that:
the invention realizes the high-strength effective connection between the zirconium alloy and the CoCrFeMnNi high-entropy alloy, and the CoCrFeNi can perform eutectic reaction with Nb (CoCrFeNi+Nb- & gtFCC+ (Co, ni) 2 Nb), the cladding layer is mainly composed of FCC matrix+ (Co, ni) 2 Nb Laves eutectic structure and Nb-based solid solution with better plasticity, wherein the eutectic structure has higher strength and plasticity, the Nb-based solid solution has better plasticity, and can serve as a transition layer in the brazing process to simultaneously reduce and release the residual stress of the joint, thereby improving the strength of the joint, and meanwhile, zr-Cu brazing filler metal forms a solid-liquid interface after being melted, and Nb reacts with Cr, mn and Zr to form (Zr, nb) (Cr, mn) at the side interface of the cladding layer and the side interface of the brazing seam 2 The plasticity of the joint connection is further improved, so that the strength of the joint is improved. Compared with the joint obtained by the traditional AgCu solder brazing zirconium alloy and CoCrFeMnNi high entropy alloy, the Zr63.2Cu36.8 solder can be used as an intermediate brazing layerThe connection between the two is effectively realized, and meanwhile, the cladding layer can be used as a transition layer in the brazing process to effectively play roles in relieving the residual stress of the joint and regulating and controlling the interface reaction, so that the strength of the joint is improved. The brittle compound in the braze joint is obviously reduced, the interface reaction is effectively regulated and controlled, and the joint performance is improved. The invention can be widely applied to CoCrFeNi-based high-entropy alloy (such as CoCrFeNiCu, coCrFeNiSn, al 0.3 CoCrFeNi, etc.) to the zirconium alloy.
Drawings
FIG. 1 is a back-scattered photograph of a cladding layer obtained in example 1 of the present invention;
FIG. 2A is a photograph of backscattering and a graph of fracture paths for a braze joint obtained in example 1 of the present invention;
FIG. 3A photograph of backscattering and a graph of fracture path for a braze joint is obtained in example 5 of the present invention;
FIG. 4 is a photograph of backscattering and a graph of fracture paths of a braze joint obtained in a comparative example of the present invention.
Detailed Description
In order to make the technical solution of the present invention better understood by those skilled in the art, the technical solution of the present invention will be clearly and completely described in the following description with reference to the accompanying drawings in the embodiments of the present invention, and all other embodiments obtained by those skilled in the art without making creative efforts based on the embodiments of the present invention are included in the scope of protection of the present invention.
A method for braze welding of high-entropy alloy and zirconium alloy by adopting laser cladding Nb comprises the following steps:
firstly, grinding a surface to be clad of the CoCrFeMnNi high-entropy alloy by using 180# metallographic sand paper, 400# metallographic sand paper, 800# metallographic sand paper, 1200# metallographic sand paper, 2000# metallographic sand paper and 3000# metallographic sand paper in sequence to obtain a base material to be clad, and preparing a cladding layer on the surface of the high-entropy alloy by using Nb powder with the laser cladding particle size of 45-105 mu m;
step two, sequentially polishing the cladding surface of the CoCrFeMnNi high entropy alloy obtained in the step one and the zirconium alloy by using 800# metallographic sand paper, 1200# metallographic sand paper, 2000# metallographic sand paper and 3000# metallographic sand paper to obtain a cladding layer and a zirconium alloy with smooth and flat surfaces, wherein a Zr63.2Cu36.8 (wt.%) eutectic alloy foil is used as a brazing filler metal;
step three, immersing the parent metal to be welded and the brazing filler metal foil obtained in the step two into an acetone solution, performing ultrasonic cleaning for 30min, and then drying, and placing in an absolute ethyl alcohol solution, performing ultrasonic cleaning for 15min, and then drying;
fourthly, placing Zr63.2Cu36.8 (wt%) solder foil between the surfaces to be welded of the high-entropy alloy and the zirconium alloy to form a sample to be welded, placing the sample to be welded in a vacuum brazing furnace, and reducing the pressure of the vacuum brazing furnace to 5x10 -3 Heating to 1010 ℃ at a speed of 10 ℃/min under Pa, preserving heat for 10min, cooling to 200 ℃ at a speed of 5 ℃/min, and finally cooling to room temperature along with the furnace.
Example 1:
step one, grinding a surface to be clad of the CoCrFeMnNi high entropy alloy by using 180# metallographic abrasive paper, 400# metallographic abrasive paper, 800# metallographic abrasive paper, 1200# metallographic abrasive paper, 2000# metallographic abrasive paper and 3000# metallographic abrasive paper sequentially to obtain a parent metal to be clad, and carrying out cladding test under the parameters of 800W laser power, 1000mm/min scanning speed and 0.3r/min powder feeding speed to obtain a cladding layer with the thickness of 370 mu m.
And step two, sequentially polishing the cladding surface of the CoCrFeMnNi high entropy alloy obtained in the step one and the zirconium alloy by using No. 800, no. 1200, no. 2000 and No. 3000 metallographic sand paper to obtain a cladding layer and the zirconium alloy with smooth and flat surfaces.
And thirdly, immersing the parent metal to be welded and the brazing filler metal foil obtained in the second step into an acetone solution, performing ultrasonic cleaning for 30min, and then drying, and then placing in an absolute ethyl alcohol solution, performing ultrasonic cleaning for 15min, and drying.
Fourthly, placing Zr63.2Cu36.8 (wt%) solder foil between the surfaces to be welded of the high-entropy alloy and the zirconium alloy to form a sample to be welded, placing the sample to be welded in a vacuum brazing furnace, and reducing the pressure of the vacuum brazing furnace to 5x10 -3 Heating to 1010 ℃ at a speed of 10 ℃/min under Pa, preserving heat for 10min, cooling to 200 ℃ at a speed of 5 ℃/min, and finally cooling to room temperature along with the furnace. At this time, the room temperature shear strength of the resulting soldered joint reached 242.8MPa.
Example 2:
the difference between this example and example 1 is that the laser powder feeding speed of 0.2 r/min is adopted in the first step. Other steps are the same as those of the specific embodiment. The thickness of the cladding layer obtained at this time was 150. Mu.m, and the shear strength of the joint reached 195.2 MPa.
Example 3:
the difference between this example and example 1 is that the laser powder feeding speed of 0.25r/min is adopted in the first step. Other steps are the same as those of the specific embodiment. The thickness of the cladding layer obtained at this time was 280. Mu.m, and the shear strength of the joint reached 225.8MPa.
Example 4:
the difference between this example and example 1 is that the laser powder feeding speed of 0.35r/min is adopted in the first step. Other steps are the same as those of the specific embodiment. The thickness of the cladding layer obtained at this time was 410. Mu.m, and the shear strength of the joint reached 201.8MPa.
Example 5:
this example differs from example 1 in that step one did not employ laser cladding and Zr63.2Cu36.8 (wt.%) braze was used to braze the HEA and Zr-3 alloys directly. Other steps are the same as those of the specific embodiment. The shear strength of the joint obtained at this time reached 172.1 MPa.
Example 6
The difference between this example and example 1 is that the laser power used in step one was 750W, respectively, and the other steps were the same as those used in the specific example, in which case the thickness of the cladding layer was 300. Mu.m, and the shear strength of the joint reached 221.3MPa.
Example 7
The difference between this example and example 1 is that the laser power used in step one was 900W, respectively, and the other steps were the same as those used in the specific example, in which case the thickness of the cladding layer was 420. Mu.m, and the shear strength of the joint reached 193.4MPa.
In other embodiments, when the laser power is low, such as 700W, the cladding layer cannot be formed, and when the laser power is high, such as 1000W, the cladding layer cannot be formed well, and the thickness of the cladding layer is considered to be 0 μm.
Comparative example: backscattering photograph and fracture path (890) of joint obtained by directly brazing zirconium alloy and CoCrFeMnNi high entropy alloy by AgCu solder in the prior art o C/10 min), it is evident from FIG. 4 that the microstructure of the linker is largely composed of a brittle reaction adjacent to the HEA sideStress layer Zr (Cr, mn) 2 Brittle Zr in the center region of the braze joint 2 (Co, cu, ni, fe), zr (Ag, cu) and Zr (Cr, mn) in bulk 2 Composition, resulting in a joint with a shear strength of only 50.2MPa. The joints being primarily broken in brittle Zr (Cr, mn) 2 In the reaction layer. Notably, due to stress concentrations, brittle Zr in the braze joint 2 Significant cracking can be observed in the (Co, cu, ni, fe) phase, which can affect the strength of the joint.
Fig. 3 is a back-scattered photograph and fracture path of a joint obtained after brazing zirconium alloy and cocrfennnni high entropy alloy directly with zr63.2cu36.8 (wt.%) (1010 o C/10 min), the microstructure of the joint consists essentially of brittle Zr (Cr, mn) adjacent to the HEA side 2 ) Zr (Cr, mn) in layers and blocks in braze joints 2 ，Zr 2 (Cu, ni, co, fe) composition, the fracture of the joint starts from HEA/Zr (Cr, mn) 2 ) At the layer interface, the crack follows the brittle Zr in the braze 2 (Cu, ni, co, fe) extension; compared with the microstructure of the joint obtained by direct brazing of AgCu braze, zrsis is derived from Zr (Cr, mn during cooling due to the large amount of Zr element being rich in braze 2 ) Layer desolventizing, resulting in Zr (Cr, mn) formed on the HEA side 2 ) A large amount of zrsis is distributed in the layer, which improves the plastic deformability of the brittle reaction layer and thus the shear strength of the joint, but a large amount of microcracks are distributed in the braze joint due to stress concentration, which affects the strength of the joint.
As can be seen from FIG. 1, when the laser power is 800W, the scanning speed is 1000mm/min, and the powder feeding speed is 0.3r/min, the thickness of the cladding layer is about 370 μm, and the microstructure is mainly composed of FCC+ (Co, ni) 2 Nb eutectic structure and residual Nb.
As can be seen from FIG. 2, during the brazing process, molten Zr-Cu braze wets and dissolves the base metal, a part of the cladding layer and Zr-3 base metal dissolve into the braze, a solid/liquid interface is formed, zr in the braze diffuses toward the cladding layer, and reacts with Nb, cr and Mn in the cladding layer to form lamellar (Zr, nb) (Cr, mn) on the side adjacent to the cladding layer 2 The method comprises the steps of carrying out a first treatment on the surface of the At the same time, nb, cr and Mn dissolved in the cladding layer in the brazing filler metal and Z in the brazing filler metalr react to form blocky (Zr, nb) (Cr, mn) in the braze joint 2 During cooling, primary (Zr, nb) 2 Cu phase is separated out from liquid phase, and the residual liquid phase is subjected to eutectic reaction to form Zrss+ (Zr, nb) 2 Cu eutectic structure and the brittle phase Zr in the joint braze joint obtained directly by brazing Zr-Cu solder 2 (Cu, ni, co, fe) and Zr (Cr, mn) 2 In contrast, the solder joint formed therein (Zr, nb) 2 Cu，(Zr,Nb)(Cr,Mn) 2 The plasticity of the phase is obviously improved, so that microcracks in the brazing seam are completely disappeared, the shearing strength of the joint is greatly improved, and the maximum is 242.8MPa.
The test results show that: when the CoCrFeMnNi high entropy alloy and the zirconium alloy are brazed by the assistance of Nb laser cladding, the brittle compound layer on the HEA side is obviously reduced; nb distributed in the cladding layer has good plasticity and smaller thermal expansion coefficient than HEA, and can simultaneously play a role in reducing and releasing the residual stress of the joint in the brazing process, thereby being beneficial to improving the strength of the joint. In addition, nb and Zr in the cladding layer can be infinitely mutually dissolved, and can play a role in regulating and controlling interface reaction, which is also beneficial to improving the strength of the joint; in the cladding layer FCC+ (Co, ni) 2 In Nb eutectic structure, FCC has good plasticity, (Co, ni) 2 The Nb phase has good strength, so that the cladding layer has good plasticity and strength, and is also beneficial to relieving the residual stress of the joint.
Claims (7)
1. A method for braze welding of high-entropy alloy and zirconium alloy by adopting laser cladding Nb is characterized by comprising the following steps:
polishing the surface of the high-entropy alloy, and preparing a cladding layer on the surface of the high-entropy alloy by cladding Nb powder with laser;
polishing and pre-treating a surface to be welded of the zirconium alloy and a surface to be welded of a cladding layer formed by the high-entropy alloy, so as to obtain a parent metal to be welded, wherein a Zr63.2Cu36.8 (wt.%) eutectic alloy foil is used as a brazing filler metal;
step three, cleaning the zirconium alloy, the high-entropy alloy and the solder foil obtained in the step three by using acetone and absolute ethyl alcohol;
fourthly, placing the Zr63.2Cu36.8 brazing foil between the surfaces to be welded of the high-entropy alloy and the zirconium alloy to form a sample to be welded, placing the sample in a vacuum brazing furnace, heating the sample to a brazing temperature of 1010 ℃ in a vacuum environment, preserving heat for 10min at the brazing temperature, and cooling to room temperature;
the high-entropy alloy is CoCrFeMnNi high-entropy alloy.
2. A method of brazing high entropy alloys and zirconium alloys with laser cladding Nb assist as claimed in claim 1, wherein: and in the first step and the second step, the surfaces to be welded of the high-entropy alloy (before and after cladding) and the zirconium alloy are polished by using 180# metallographic sand paper, 400# metallographic sand paper, 800# metallographic sand paper, 1200# metallographic sand paper, 2000# metallographic sand paper and 3000# metallographic sand paper.
3. A method of brazing high entropy alloys and zirconium alloys with laser cladding Nb assist as claimed in claim 1, wherein: in the first step, nb powder is laser cladding, and the thickness of a cladding layer formed on the surface of the high-entropy alloy is 150-420 mu m.
4. A method of brazing high entropy alloys and zirconium alloys with the assistance of Nb using laser cladding according to claim 3, wherein: in the first step, the particle diameter of Nb is 45-105 mu m, and the parameters of laser cladding are 750-900W, the scanning speed is 1000mm/min and the powder feeding speed is 0.2-0.35r/min.
5. A method of brazing high entropy alloys and zirconium alloys with laser cladding Nb assist as claimed in claim 1, wherein: in the second step, the thickness of the Zr63.2Cu36.8 solder foil is 200 μm.
6. A method of brazing high entropy alloys and zirconium alloys with laser cladding Nb assist as claimed in claim 1, wherein: and in the third step, the zirconium alloy, the high-entropy alloy and the Zr63.2Cu36.8 solder foil are firstly ultrasonically cleaned for 30min by using acetone, then ultrasonically cleaned for 15min by using absolute ethyl alcohol, and dried.
7. According to claimThe method for brazing high-entropy alloy and zirconium alloy by adopting laser cladding Nb is characterized in that: the vacuum heating in the fourth step is 5×10 -3 Heating under the vacuum condition of Pa or below, heating to brazing temperature at the speed of 10 ℃/min, preserving heat, cooling to 200 ℃ at the speed of 5 ℃/min after brazing, and finally cooling to room temperature along with a furnace.
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|---|---|---|---|
| CN202311430220.3A CN117259885A (en) | 2023-10-31 | 2023-10-31 | Method for brazing zirconium alloy and high-entropy alloy by adopting laser cladding Nb |
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|---|---|---|---|
| CN202311430220.3A CN117259885A (en) | 2023-10-31 | 2023-10-31 | Method for brazing zirconium alloy and high-entropy alloy by adopting laser cladding Nb |
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