CN114799395B - Vacuum brazing method for dissimilar nickel-based high-temperature alloy for improving strength stability of joint - Google Patents
Vacuum brazing method for dissimilar nickel-based high-temperature alloy for improving strength stability of joint Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/008—Soldering within a furnace
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- 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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- 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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3033—Ni as the principal constituent
- B23K35/304—Ni as the principal constituent with Cr as the next major constituent
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Abstract
A vacuum brazing method for dissimilar nickel-based high-temperature alloys for improving the strength stability of joints belongs to the technical field of high-temperature alloy welding. The method comprises the following steps: cleaning the surface of the alloy and cleaning the part to be welded; assembling and positioning by adopting an energy storage welding method; heating the components to be welded to 600-700 ℃ and preserving heat, then heating to 850-950 ℃ and preserving heat, and then heating to 1050-1070 ℃ and preserving heat for 10-15min for vacuum brazing; and heating the welded assembly to 1010-1040 ℃, preserving heat for 3-5h for homogenization treatment, and then carrying out oil quenching and cooling to room temperature. The method eliminates the hard brittle phase in the central area of the welding line, completely generates solid solution tissues in the welding line and obviously improves the uniformity of the microstructure. The process has unexpected effects in the aspects of improving the strength uniformity and stability of the joint, is particularly suitable for the brazing joint with the gap value of 60-150 mu m, and has great popularization value. The test results of multiple groups of mechanical properties show that the standard difference of the shear strength and the tensile strength of the joint treated by the process disclosed by the invention at 730 ℃ is reduced by more than 70%.
Description
Technical Field
The invention relates to a vacuum brazing method for dissimilar nickel-based high-temperature alloy for improving the strength stability of a joint, and belongs to the technical field of high-temperature alloy welding.
Background
An aircraft engine is a very representative high-precision technical product, and the heart of the aircraft is the key for promoting the development and the progress of the national aviation industry. The hot end component is the key component of the core of the aircraft engine. The parts need to work stably for a long time under the complex and severe environments of high temperature, corrosion, stress, vibration and the like, and the performance directly determines the weight ratio and the working efficiency of the engine. The hot end parts of the current engines are mainly made of high temperature alloys, especially mainly nickel-based high temperature alloys.
The nickel-based high-temperature alloy has various types, and the performance and the characteristics of the alloys with different grades are different. The GH3536 alloy belongs to solid solution strengthening type nickel-based deformation high-temperature alloy, has excellent cold and hot processing formability and welding performance, and has good oxidation resistance and mechanical property below 900 ℃. The GH4738 alloy belongs to gamma' phase precipitation strengthening type nickel-based deformation high-temperature alloy, and has the outstanding characteristics of excellent toughness matching and structural stability, and higher yield strength and fatigue crack propagation resistance between 760 ℃ and 870 ℃. With the increasing performance of aircraft engines, the requirements for structural complexity and service performance of high temperature alloy components have become more stringent. The reliable connection between the nickel-based wrought superalloy with different grades can be realized, the respective advantages can be fully exerted, and the method has important practical significance for promoting the technical progress of the engine.
The welding technology can quickly realize the connection of two parts, and is widely applied in the field of high-temperature alloys. The fusion welding process such as laser welding, arc welding and the like can be carried out at room temperature or under special conditions, welding equipment is simple, however, fusion welding needs to locally melt the base metal, the welding temperature is high, the thermal stress value after welding is large, and the microstructure uniformity of the base metal can be reduced. In contrast, the vacuum brazing heating temperature is relatively low, the base metal does not need to be melted, the joint surface is smooth and clean, the air tightness is good, and the same or different metals can be connected. In addition, the quality of the alloy surface after welding is high due to welding in a vacuum environment. The current vacuum brazing is a key manufacturing process technology of the high-temperature alloy part, and the future application prospect is wide.
Setting the gap value to a small range is difficult and expensive to achieve in view of sample size and assembly accuracy during vacuum brazing. Taking the GH3536 and GH4738 alloy brazed components processed by the traditional vacuum brazing process as an example, when the joint gap value exceeds 60 mu m, large-area hard and brittle phases such as boride and the like are easily generated at the center of a welding seam, so that the toughness of the joint is seriously reduced, and the strength values of the joint are uneven and change greatly. Therefore, it is necessary to develop a vacuum brazing method for dissimilar nickel-based superalloy for improving strength stability of a joint, so as to improve service stability and safety of a brazed assembly.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide a vacuum brazing method for dissimilar nickel-based high-temperature alloys, which is used for improving the strength stability of joints, so as to realize more stable connection among the alloys.
In order to achieve the purpose, the invention provides the following technical scheme: the vacuum brazing method of dissimilar nickel-based high temperature alloy for improving the strength stability of the joint comprises the following steps:
step one, preparing before welding: removing oxide skin on the surface of the alloy by a mechanical method until the metallic luster is exposed, then polishing the surface by 1500# abrasive paper, and sequentially cleaning the part to be welded by acetone and alcohol;
step two, assembling and positioning: sandwiching an intermediate layer alloy between prepared alloys to be welded to form a brazing assembly of a sandwich structure, and then fixing the alloys to be welded by using energy storage electric welding and compressing the alloys; the interlayer alloy is foil-shaped amorphous nickel-based brazing filler metal and has the thickness of 60-150 mu m;
step three, furnace charging and brazing: putting the assembled components to be welded into a vacuum brazing furnace and vacuumizing to 10 DEG -3 Pa below; heating to 600-700 deg.C at a rate of 5-15 deg.C/min, and maintaining for 10-20min; heating to 850-950 deg.C at a rate of 5-15 deg.C/min, and maintaining for 20-30min; heating to 1050-1070 ℃ at the speed of 5-10 ℃/min, and carrying out vacuum brazing after heat preservation for 10-15 min; the welded assembly is cooled in a sectional mode, the assembly is cooled to 900 ℃ along with the furnace at the speed of 4 ℃/min, and then high-purity nitrogen is introduced into the furnace to rapidly cool the assembly to room temperature and then the assembly is discharged;
step four, homogenizing treatment: and (3) placing the welded assembly in a heating furnace, heating to 1010-1040 ℃ at the speed of 15-30 ℃/min, preserving heat for 3-5h, and then performing oil quenching and cooling to room temperature.
Further, the dissimilar nickel-based superalloy is a solid solution strengthening type GH3536 alloy and a gamma' phase precipitation strengthening type GH4738 alloy.
Further, the nickel-based brazing filler metal in the second step is BNi-2 brazing filler metal, the melting point is 980-1000 ℃, and the nickel-based brazing filler metal comprises the following components in percentage by mass: b:2.75-3.5%, si:4-5%, cr:6-8%, fe:2.5-3.5%, ni: and (4) the balance.
Further, the temperature is raised in stages before the brazing in step three to make the brazed assembly heated more uniformly.
Compared with the prior art, the invention has the beneficial effects that:
1) The invention promotes the mutual diffusion of elements between the brazing filler metal and the alloy base metal by properly increasing the brazing heat preservation temperature, prolonging the brazing heat preservation time and matching with the post-welding homogenization treatment; the hardness and brittleness of the central area of the welding seam are eliminated after treatment, solid solution tissues are completely generated inside the welding seam, and the uniformity of the microstructure is obviously improved. The process has unexpected effects on improving the strength uniformity and stability of the joint, and lays a foundation for the long-time reliable and stable operation of the vacuum brazing assembly. After treatment, standard deviations of the shear strength and the tensile strength of the soldered joint under a high-temperature condition are respectively 8.0 MPa and 7.5MPa, and can be respectively reduced by 72 percent and 78 percent compared with the soldered joint before process optimization.
2) The homogenization treatment temperature of the invention is close to the complete re-dissolution temperature of the gamma' phase in the GH4738 alloy, and the homogenization treatment is followed by cooling in an oil quenching way. Therefore, the treatment achieves the aim of solution treatment of the GH4738 alloy while homogenizing the internal structure of the weld joint, and lays a good foundation for subsequent further aging treatment.
3) The invention has simple process operation, low requirement on equipment, high application and popularization value and is particularly suitable for the brazing connection process with the joint clearance value in the range of 60-150 mu m; the similar method can be popularized to other dissimilar nickel-based high-temperature alloy systems.
Drawings
FIG. 1 shows the microstructure of the joint region after treatment according to the procedure described in example 1.
FIG. 2 shows the microstructure of the joint region after treatment according to the process described in comparative example 1.
Detailed Description
Although the existing vacuum brazing method can realize the quick connection of nickel-based high-temperature alloys of different brands, when the gap of a joint is slightly large, a large area of hard and brittle phases such as boride are easily generated at the center of the weld joint, so that the strength value of the joint greatly fluctuates.
The invention obtains a novel vacuum brazing method for dissimilar nickel-based high-temperature alloy for improving the strength stability of a joint through a large number of tests and grope. Wherein, the dissimilar nickel-based high-temperature alloy for vacuum brazing is a solid solution strengthening GH3536 alloy and a gamma' phase precipitation strengthening GH4738 alloy respectively; the brazing filler metal is BNi-2 nickel-based brazing filler metal, contains alloy elements such as Cr, fe, si, B and the like, and has a melting point of 980-1000 ℃; the size of the joint gap is 60-150 mu m, and the specific gap value is controlled by the thickness of the foil-shaped amorphous nickel-based brazing filler metal. The brazing method comprises the following steps:
the method comprises the following steps: removing oxide skin on the surface of the alloy to be welded by a mechanical method until the metallic luster is exposed, then polishing the surface by 1500# abrasive paper, and sequentially cleaning the part to be welded by acetone and alcohol.
The purpose of this step is to ensure that the alloy surface is smooth, free of scale, oil and other impurities prior to welding.
Step two: and a foil-shaped brazing filler metal is clamped between the alloys to be welded to form a brazing assembly with a sandwich structure, and then the alloys are fixed and compressed by energy storage electric welding.
The purpose of this step is to fix the alloy and prevent the size of the joint gap from deviating during the welding process.
Step three: putting the assembled components to be welded into a vacuum brazing furnace and vacuumizing to 10 DEG -3 Pa below; heating to 600-700 deg.C at a rate of 5-15 deg.C/min, and maintaining for 10-20min; heating to 850-950 deg.C at a rate of 5-15 deg.C/min, and maintaining for 20-30min; heating to 1050-1070 ℃ at the speed of 5-10 ℃/min, and carrying out vacuum brazing after heat preservation for 10-15 min; and cooling the welded assembly to 900 ℃ along with the furnace at the speed of 4 ℃/min, introducing high-purity nitrogen into the furnace to quickly cool the assembly to room temperature, and discharging.
The main purpose of the step is to improve the brazing temperature and time on the premise of ensuring that the base metal alloy is not obviously corroded, further increase the solid solution structure content in the welding seam and reduce the precipitation amount of brittle phases such as boride in a central area. In addition, this step of raising the temperature in stages may allow the brazed assembly to be heated more uniformly. In the cooling stage, furnace slow cooling is firstly carried out to slow down the solidification rate, so that the welding thermal stress is reduced; the purpose of introducing nitrogen for quick cooling is to reduce the influence of high temperature and long-time exposure on the microstructure of the alloy and improve the production efficiency.
Step four: and (3) placing the welded assembly in a heating furnace, heating to 1010-1040 ℃ at the speed of 15-30 ℃/min, preserving heat for 3-5h, and then performing oil quenching and cooling to room temperature.
The purpose of the step is to promote the mutual diffusion of elements between the parent metal and the welding seam through the long-time heat preservation under the high-temperature condition, so that harmful phases such as boride in the central area of the welding seam are fully decomposed and disappeared, and the uniformity of the welding seam structure is improved. The homogenization treatment temperature is close to the complete re-dissolution temperature of the gamma' phase in the GH4738 alloy, and oil quenching is performed after homogenization, so that the aim of solution treatment of the involution Jin Mucai is fulfilled while the microstructure in the welding line is homogenized, and a foundation is laid for the subsequent aging treatment.
The present invention will be described in further detail with reference to examples. The embodiment takes the size as
The GH3536 and GH4748 alloy samples are used as examples for illustration, the welding surfaces are round end surfaces, and the components of the brazing filler metal are shown in the following table 1.
TABLE 1 example BNi-2 Nickel-based brazing filler metal composition (wt.%)
| Composition (A) | Cr | B | Si | Fe | Ni |
| Content (wt.) | 6.9 | 3.1 | 4.5 | 3.1 | Balance of |
Example 1
The method comprises the following steps: removing oxide skin on the surface of the alloy by a mechanical method until the metallic luster is exposed, then polishing the surface by 1500# abrasive paper, and sequentially cleaning the part to be welded by acetone and alcohol;
step two: foil-shaped brazing filler metal with the thickness of 100 mu m is clamped between prepared alloys to be welded to form a brazing assembly with a sandwich structure, and then the alloys to be welded are fixed and compressed by energy storage electric welding;
step three: putting the assembled components to be welded into a vacuum brazing furnace and vacuumizing to 10 DEG -3 Pa below; heating to 650 ℃ at the speed of 15 ℃/min, and keeping the temperature for 12min; heating to 870 ℃ at the speed of 10 ℃/min, and keeping the temperature for 20min; heating to 1050 ℃ at the speed of 8 ℃/min, and carrying out vacuum brazing after heat preservation for 15min; cooling the welded assembly to 900 ℃ along with the furnace at the speed of 4 ℃/min, introducing high-purity nitrogen into the furnace to quickly cool the assembly to room temperature, and discharging;
step four: and (3) placing the welded assembly in a heating furnace, heating to 1020 ℃ at the speed of 20 ℃/min, preserving the temperature for 4h, and then carrying out oil quenching and cooling to room temperature.
As shown in figure 1, the internal structure of the weld joint is relatively uniform after the process is carried out, and no other obvious precipitated phases exist in the central area.
Example 2
The method comprises the following steps: removing oxide skin on the surface of the alloy by a mechanical method until the metallic luster is exposed, then polishing the surface by 1500# abrasive paper, and sequentially cleaning the part to be welded by acetone and alcohol;
step two: foil-shaped brazing filler metal with the thickness of 110 mu m is clamped between prepared alloys to be welded to form a brazing assembly with a sandwich structure, and then the alloys to be welded are fixed and compressed by energy storage electric welding;
step three: putting the assembled components to be welded into a vacuum brazing furnace and vacuumizing to 10 DEG -3 Pa below; heating to 700 deg.C at a rate of 12 deg.C/min, and maintaining for 15min; heating to 900 deg.C at a rate of 15 deg.C/min, and maintaining for 25min; heating to 1060 ℃ at the speed of 5 ℃/min, and keeping the temperature for 12min for vacuum brazing; cooling the welded assembly to 900 ℃ along with the furnace at the speed of 4 ℃/min, introducing high-purity nitrogen into the furnace to quickly cool the assembly to room temperature, and discharging;
step four: and (3) placing the welded assembly in a heating furnace, heating to 1030 ℃ at the speed of 15 ℃/min, preserving the temperature for 5h, and then carrying out oil quenching and cooling to room temperature.
Comparative example 1
The method comprises the following steps: removing oxide skin on the surface of the alloy by using a mechanical method until the metallic luster is exposed, then polishing the surface by using 1500# abrasive paper, and sequentially cleaning the part to be welded by using acetone and alcohol;
step two: foil-shaped brazing filler metal with the thickness of 100 mu m is clamped between prepared alloys to be welded to form a brazing assembly with a sandwich structure, and then the alloys to be welded are fixed and compressed by energy storage electric welding;
step three: putting the assembled components to be welded into a vacuum brazing furnace and vacuumizing to 10 DEG -3 Pa below; heating to 850 deg.C at a rate of 15 deg.C/min, and maintaining for 25min; heating to 1030 ℃ at the speed of 8 ℃/min, and carrying out vacuum brazing after heat preservation for 8 min; cooling the welded assembly to 900 ℃ along with the furnace at the speed of 4 ℃/min, introducing high-purity nitrogen into the furnace to quickly cool the assembly to room temperature, and discharging;
compared with the microstructure of the joint area treated by the process described in example 1, the weld joint treated by the process has large-area hard and brittle phases such as boride in the central area of the weld joint (as shown in fig. 2).
Performance detection
The samples subjected to the vacuum brazing process in example 1 and comparative example 1 were subjected to a shear strength test at 730 c, and the test results are shown in table 2.
TABLE 2 test results for shear strength of joints
| Sample (I) | Shear strength/MPa | Standard deviation value/MPa |
| Example 1 | 225、219、208、228、206、217、226、211 | 8.0 |
| Comparative example 1 | 238、168、169、182、188、217、239、233 | 28.8 |
Tensile strength tests were performed at 730 ℃ on the samples subjected to the vacuum brazing process in example 1 and comparative example 1, and the test results are shown in table 2.
TABLE 3 tensile Strength test results for joints
| Sample (I) | Tensile strength/MPa | Standard deviation value/MPa |
| Example 1 | 259、271、269、281、278、283、274、266 | 7.5 |
| Comparative example 1 | 280、270、265、235、265、172、223、219 | 33.8 |
In tables 2 and 3, comparative example 1 is the GH3536/GH4738 joint strength measured after processing by the conventional vacuum brazing process, while example 1 is the GH3536/GH4738 joint strength measured after processing by the process of the present invention. The test result shows that the strength stability of the joint is obviously improved after the process is adopted for treatment, the standard difference value of the strength of the joint is reduced by more than 70 percent, and the technical problem of poor strength stability of the joint in the actual production process is solved.
In addition to the above, other embodiments of the present invention are possible. All technical solutions which adopt equivalent substitutions or equivalent transformations fall within the protection scope of the claims of the present invention.
Claims (2)
1. A vacuum brazing method for dissimilar nickel-based high-temperature alloy for improving strength stability of joints is characterized by comprising the following steps:
step one, preparing before welding: removing oxide skin on the surface of the alloy by a mechanical method until the metallic luster is exposed, then polishing the surface by 1500# abrasive paper, and sequentially cleaning the part to be welded by acetone and alcohol;
step two, assembling and positioning: sandwiching an intermediate layer alloy between prepared alloys to be welded to form a brazing assembly of a sandwich structure, and then fixing the alloys to be welded by using energy storage electric welding and compressing the alloys; the interlayer alloy is foil-shaped amorphous nickel-based brazing filler metal and has the thickness of 60-150 mu m;
step three, furnace charging and brazing: putting the assembled components to be welded into a vacuum brazing furnace and vacuumizing to 10 DEG -3 Pa below; heating to 600-700 deg.C at a rate of 5-15 deg.C/min, and maintaining for 10-20min; at 5-15Heating to 850-950 deg.C at a rate of 850/min, and maintaining the temperature for 20-30min; heating to 1050-1070 ℃ at the speed of 5-10 ℃/min, and carrying out vacuum brazing after heat preservation for 10-15 min; the welded assembly is cooled in a sectional mode, the assembly is cooled to 900 ℃ along with the furnace at the speed of 4 ℃/min, and then high-purity nitrogen is introduced into the furnace to rapidly cool the assembly to room temperature and then the assembly is discharged;
step four, homogenizing treatment: placing the welded assembly in a heating furnace, heating to 1010-1040 ℃ at the speed of 15-30 ℃/min, preserving heat for 3-5h, and then carrying out oil quenching and cooling to room temperature;
the dissimilar nickel-based high-temperature alloy is a solid solution strengthening type GH3536 alloy and a gamma' phase precipitation strengthening type GH4738 alloy;
the nickel-based brazing filler metal in the second step is BNi-2 brazing filler metal, the melting point is 980-1000 ℃, and the nickel-based brazing filler metal comprises the following components in percentage by mass: b:2.75-3.5%, si:4-5%, cr:6-8%, fe:2.5-3.5%, ni: and the balance.
2. The method of vacuum brazing dissimilar nickel based superalloys to improve joint strength stability as claimed in claim 1 wherein the temperature is raised in stages prior to step three to make the brazed assembly more uniformly heated.
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