CN114833410B - Method for reducing residual stress of heterogeneous brazed joint - Google Patents
Method for reducing residual stress of heterogeneous brazed joint Download PDFInfo
- Publication number
- CN114833410B CN114833410B CN202210780917.2A CN202210780917A CN114833410B CN 114833410 B CN114833410 B CN 114833410B CN 202210780917 A CN202210780917 A CN 202210780917A CN 114833410 B CN114833410 B CN 114833410B
- Authority
- CN
- China
- Prior art keywords
- temperature
- cooling
- residual stress
- brazing
- heating
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 238000000034 method Methods 0.000 title claims abstract description 40
- 238000001816 cooling Methods 0.000 claims description 103
- 239000000463 material Substances 0.000 claims description 64
- 238000005219 brazing Methods 0.000 claims description 62
- 238000010438 heat treatment Methods 0.000 claims description 46
- 229910052751 metal Inorganic materials 0.000 claims description 18
- 239000002184 metal Substances 0.000 claims description 18
- 239000000919 ceramic Substances 0.000 claims description 15
- 239000000945 filler Substances 0.000 claims description 15
- 238000004321 preservation Methods 0.000 claims description 10
- 229910000851 Alloy steel Inorganic materials 0.000 claims description 8
- 229910000975 Carbon steel Inorganic materials 0.000 claims description 8
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 8
- 239000010962 carbon steel Substances 0.000 claims description 8
- 229910000679 solder Inorganic materials 0.000 claims description 8
- 238000005476 soldering Methods 0.000 claims description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 4
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 claims description 4
- 229910052709 silver Inorganic materials 0.000 claims description 4
- 239000004332 silver Substances 0.000 claims description 4
- 229910000838 Al alloy Inorganic materials 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 2
- 229910052782 aluminium Inorganic materials 0.000 claims description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 2
- 239000010949 copper Substances 0.000 claims description 2
- 229910052802 copper Inorganic materials 0.000 claims description 2
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 229910052725 zinc Inorganic materials 0.000 claims description 2
- 239000011701 zinc Substances 0.000 claims description 2
- 238000003466 welding Methods 0.000 abstract description 5
- 229920000426 Microplastic Polymers 0.000 abstract description 2
- 230000008602 contraction Effects 0.000 abstract description 2
- 238000001556 precipitation Methods 0.000 abstract description 2
- 210000005067 joint tissue Anatomy 0.000 abstract 1
- 210000001519 tissue Anatomy 0.000 abstract 1
- 229910001220 stainless steel Inorganic materials 0.000 description 26
- 239000010935 stainless steel Substances 0.000 description 26
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 18
- 230000000052 comparative effect Effects 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 239000010953 base metal Substances 0.000 description 5
- 238000001000 micrograph Methods 0.000 description 4
- 208000013201 Stress fracture Diseases 0.000 description 3
- 238000004140 cleaning Methods 0.000 description 2
- 230000001595 contractor effect Effects 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 208000010392 Bone Fractures Diseases 0.000 description 1
- 206010017076 Fracture Diseases 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 150000002894 organic compounds Chemical class 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
Images
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
-
- 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
- B23K37/00—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups
- B23K37/003—Cooling means
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Optics & Photonics (AREA)
- Ceramic Products (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The invention belongs to the technical field of welding, and relates to a method for reducing residual stress of a heterogeneous brazed joint. When the temperature of the soldered joint is reduced to a certain temperature, the temperature is firstly raised to generate micro plastic deformation and micro precipitation, the residual stress is reduced, the temperature is reduced again to generate the residual stress, the stress is reduced by raising the temperature, the temperature of the joint is reduced in the circulating process, and the residual stress of the joint is reduced at the same time. The cryogenic cycle treatment of the invention eliminates movable dislocation in the tissue by uneven deformation caused by expansion with heat and contraction with cold through temperature rise and fall cycles between (0.1 to 0.4) T and (75 to 150) DEG C, fixes dislocation entanglement and increment, and reduces residual stress in the soldered joint tissue.
Description
Technical Field
The invention belongs to the technical field of welding, and relates to a method for reducing residual stress of a heterogeneous brazed joint.
Background
After the brazing of the heterogeneous material brazing joint is completed, the heterogeneous material with small shrinkage can prevent the heterogeneous material with large shrinkage from continuously shrinking, the heterogeneous material with large shrinkage can receive tensile stress along the direction of a brazing interface at the moment, and the heterogeneous material with small shrinkage can receive compressive stress along the direction of the brazing interface, so that large residual stress is easily generated on the interface after the brazing joint is welded, cracks or other types of defects occur in the joint, and the bonding strength and the service life are reduced.
Moreover, in the process of cooling the joint, because the residual stress is generated due to the uneven deformation and the phase change deformation caused by the uneven cooling and the different linear expansion coefficients, the strength and the stress fracture resistance of the joint are greatly reduced, and a novel cooling treatment method capable of reducing the residual stress of the joint and improving the comprehensive performance of the joint is urgently needed.
Disclosure of Invention
The invention aims to provide a method for greatly reducing the residual stress of a heterogeneous brazed joint aiming at the problems in the prior art.
The purpose of the invention can be realized by the following technical scheme: a method of reducing residual stress of a heterogeneous brazed joint, the method comprising brazing, the brazing comprising a temperature-raising, holding, and cooling cycle process, the cooling cycle process comprising: and (3) performing at least 2 cycles of cooling, heat preservation, heating and heat preservation, wherein the temperature after cooling is not higher than the temperature after cooling in the previous cooling cycle, and the temperature after heating is not higher than the temperature after heating in the previous cooling cycle.
In the method for reducing the residual stress of the heterogeneous soldered joint, in the cooling cycle treatment process, the temperature after cooling in the first cooling cycle is (0.5 to 0.7) Ts, the temperature after heating is (0.7 to 0.9) Ts, the temperature after cooling in the last cooling cycle is (0.1 to 0.2) Ts, the temperature after heating is (0.15 to 0.3) Ts, and Ts is the solidus temperature of the solder.
Compared with the traditional cooling treatment mode, in the cooling process of the joint, the structural distortion of the joint is caused by uneven cooling, phase change and the like, so that a large amount of residual stress is generated on the joint.
Preferably, in the cooling cycle treatment, the temperature after cooling in the first cooling cycle is (0.6 to 0.7) Ts, and the temperature after reheating is (0.8 to 0.9) Ts: the temperature after cooling in the last cooling cycle is (0.1 to 0.2) Ts, and the temperature after heating is (0.2 to 0.3) Ts.
In the method for reducing the residual stress of the heterogeneous brazed joint, the method further comprises cryogenic circulation treatment after cooling circulation treatment, wherein the cryogenic circulation treatment comprises at least 2 cycles of cooling, heat preservation, heating and heat preservation, and the temperature after cooling in the cryogenic circulation treatment is T 1 The temperature after temperature rise is T 2 ，T 1 The range is (75 to 150) DEG C, T 2 The range is (0.2 to 0.3) Ts, and the temperature is reduced to T in the last cycle 1 And then preserving heat, heating to room temperature or cooling to room temperature after the last circulation is finished, wherein Ts is the solidus temperature of the brazing filler metal.
Preferably, the cooling rate in the cooling cycle treatment and the cooling rate in the deep cooling cycle treatment are both 5 to 20 ℃/min.
Preferably, the holding time in the cooling cycle treatment and the deep cooling cycle treatment is 1 to 5 hours. The two heat preservation times of a single circulation in the cooling circulation treatment or the deep cooling circulation treatment can be the same or different.
Preferably, the temperature rise rate in the cooling cycle treatment and the deep cooling cycle treatment is 5 to 20 ℃/min.
The cryogenic cycle treatment of the invention eliminates movable dislocation in the tissue by the uneven deformation caused by the expansion and contraction effect of heat through the temperature rise and fall cycle treatment between (0.1 to 0.4) Ts and (75 to 150) DEG C, fixes dislocation entanglement and increment, and reduces the residual stress in the tissue.
The invention can greatly reduce the residual stress of the soldered joint through two-stage cooling treatment, and improve the strength and the stress fracture resistance of the joint.
In the method for reducing the residual stress of the heterogeneous soldered joint, the soldering specifically includes soldering and connecting the first base material and the second base material by using a solder, and the soldering and connecting satisfy the following calculation formula:
wherein alpha is 1 Is a first base material expansion coefficient, T is a solder joint welding temperature, sigma 1 To apply stresses parallel to the brazing interface of the first base material, E 1 Is the first parent material elastic modulus, alpha 2 Is the second parent material expansion coefficient, sigma 2 To apply stress parallel to the brazing interface of the second base material, E 2 The second base material elastic modulus, t is room temperature.
As a matter of preference,
。
it is further preferable that the concentration of the organic compound,
。
it is still further preferred that,
。
under the condition of room temperature of 20 ℃, a first parent metal and a second parent metal of the heterogeneous material have the same length L and have different linear expansion coefficients, and the linear expansion coefficient of the first parent metal is alpha 1 The linear expansion coefficient of the second base material is alpha 2 ，α 1 Greater than alpha 2 At the time of brazing, the first base material and the second base material are addedHeating to brazing temperature T, wherein the linear expansion amounts of the two are respectively Delta L 1 /L=α 1 ×（T-20），ΔL 2 /L =α 2 ×（T-20），ΔL 1 /L is greater than Δ L 2 and/L, after brazing with the brazing filler metal, forming an integral joint by the first base material and the second base material, and theoretically, respectively generating linear shrinkage delta L when the first base material and the second base material are cooled to room temperature 1 /L =α 1 ×（T-20），ΔL 2 /L =α 2 X (T-20), but the first base material and the second base material form an integral body after welding, the second base material with a small shrinkage prevents the first base material from continuing to shrink, and at this time, the first base material receives tensile stress in the direction of the brazing interface, and the second base material receives compressive stress in the direction of the brazing interface, so that residual stress occurs after the brazed joint is welded. The elastic modulus of the invention is E when heating 1 First base material and elastic modulus of E 2 Second base material applying prestress sigma 1 And prestress σ 2 . The wire deformation amount of the first base material is DeltaL 1 /L =α 1 ×（T-20）+σ 1 /E 1 Prestressed σ 1 For compressive stress, the line is deformed by an amount Δ L 1 the/L is reduced. The linear deformation amount of the second base material is DeltaL 2 /L =α 2 ×（T-20）+σ 2 /E 2 Prestressing σ 1 The wire is deformed by an amount DeltaL for tensile stress 2 increasing/L, and finally controlling to enable the linear deformation of the two to be close to each other, thereby achieving the purpose of reducing the residual stress after the joint is welded.
Preferably, when σ is 1 In case of =0, the brazed joint satisfies the following calculation formula:
preferably, when σ is 2 In case of =0, the brazed joint satisfies the following calculation formula:
due to the elastic modulus when heatedIs E 1 First base material and elastic modulus of E 2 Second base material applying prestress sigma 1 And prestress σ 2 The invention can also apply stress to one of the base metals during heating to enable the linear deformation of the base metals to be close to each other, thereby achieving the purpose of reducing the residual stress after the joint is welded.
In the above method for reducing the residual stress of the heterogeneous soldered joint, the solder comprises at least one of nickel-based, copper-based, silver-based, aluminum-based, zinc-based and tin-based solders.
In the above method of reducing residual stress of the dissimilar brazed joint, the first base material includes at least one of carbon steel, alloy steel, aluminum alloy, and copper alloy.
In the above method of reducing the residual stress of the dissimilar brazed joint, the second base material includes at least one of cemented carbide, ceramic, carbon steel, alloy steel, and copper alloy.
Preferably, when the first base material is carbon steel, the second base material is one of cemented carbide, ceramics, alloy steel, and copper alloy.
Preferably, when the first base material is alloy steel, the second base material is one of cemented carbide, ceramics, carbon steel, and copper alloy.
Preferably, when the first base material is an aluminum alloy, the second base material is one of a cemented carbide, a ceramic, a carbon steel, an alloy steel, and a copper alloy.
Preferably, when the first base material is a copper alloy, the second base material is one of cemented carbide, ceramics, carbon steel, and alloy steel.
In the method for reducing the residual stress of the heterogeneous brazed joint, the welding surface of the first base material or the second base material comprises at least one of a groove and a hole.
In one of the above-described methods of reducing residual stress of a heterogeneous brazed joint, the groove or hole cross-section includes at least one of an arc and a square.
According to the invention, the grooves or the holes are processed on the brazing surface of the first base material or the second base material, the cross sections of the grooves or the holes can be arc or square, and the grooves or the holes can cut off the stress integrity generated in the cooling shrinkage deformation process, so that the residual stress is reduced.
Compared with the prior art, the invention has the following beneficial effects:
1. when the temperature of the joint is reduced to a certain temperature, the joint is subjected to temperature rise treatment firstly to generate micro plastic deformation and micro precipitation, the residual stress is reduced, the residual stress is generated after the temperature is reduced again, the stress is reduced by temperature rise again, the temperature of the joint is reduced gradually in the circulating process, and compared with the traditional temperature reduction treatment mode, the joint temperature reduction device can greatly reduce the residual stress of the joint;
2. the cryogenic circulation treatment of the invention utilizes the temperature rise and drop circulation between (0.1 to 0.4) T and (75 to 150) DEG C to eliminate the movable dislocation in the tissue due to the uneven deformation generated by the effect of expansion caused by heat and contraction caused by cold, fix the dislocation entanglement and increment, and reduce the residual stress in the tissue of the soldered joint;
3. the invention has the elasticity modulus E when being heated 1 First base material and elastic modulus of E 2 Second base material applying prestress sigma 1 And prestress σ 2 Finally, the linear deformation of the two components is close to each other during brazing, so that the purpose of reducing the residual stress of the welded joint is achieved;
4. according to the invention, the integrity of the stress generated in the process of cutting, cooling and shrinking deformation is reduced by arranging the grooves or holes on the brazing surfaces of the first base metal and the second base metal, so that the residual stress is reduced.
Drawings
FIG. 1 is an electron microscope image of the brazing interface of a 316L stainless steel and alumina ceramic brazing sample of example 5; in the figure, 100, alumina ceramics, 200, 316L stainless steel, 300, ag71Cu26Ti3 brazing filler metal.
FIG. 2 is a macroscopic picture and an electron microscope picture of the surface of the alumina ceramic of the 316L stainless steel and alumina ceramic brazing sample in the comparative example 2.
FIG. 3 is an electron microscope image of the brazing interface of 316L stainless steel and alumina ceramic brazing sample in comparative example 2 at different magnifications; in the figure, 100, alumina ceramics, 200, 316L stainless steel, 300, ag71Cu26Ti3 brazing filler metal.
FIG. 4 is a schematic view of a cooling cycle process in brazing according to example 1.
FIG. 5 is a schematic view of a cryogenic cycle treatment in brazing according to example 1.
FIG. 6 is a schematic view of a trench according to example 7; 1. YG20 cemented carbide, 200, 316L stainless steel, 3, groove.
Detailed Description
The following are specific examples of the present invention and further describe the technical solutions of the present invention, but the present invention is not limited to these examples.
Example 1:
s1, setting the expansion coefficient as alpha 1 =18×10 -6 /. Degree.C.and elastic modulus E 1 316L stainless steel of =206GPa, the expansion coefficient is alpha 2 =6×10 -6 /. Degree.C.and elastic modulus E 2 And (3) grinding and ultrasonically cleaning the YG20 hard alloy with the hardness of =14.5GPa to remove surface scale and impurities.
S2, respectively coating silver brazing agents on brazing surfaces of 316L stainless steel and YG20 hard alloy, then adding BAg65CuZn brazing filler metal on a brazing interface at 750 ℃, preserving heat for 5min after the brazing filler metal is molten, cooling and reducing stress of a brazed joint, and checking the national standard GB/T10046-2018 silver brazing filler metal, wherein the solidus line temperature of the brazing filler metal BAg65CuZn used in the embodiment is = Ts 670 ℃;
the brazed joint after the brazing connection is subjected to cooling circulation treatment as shown in fig. 4, and the cooling circulation treatment specifically comprises the following steps:
(1) Cooling to 0.6Ts =402 ℃ at a cooling rate of 10 ℃/min for 2h, and then heating to 0.8Ts =536 ℃ at a heating rate of 10 ℃/min for 2h.
(2) The soldered joint is cooled to 0.5Ts =335 ℃ at the cooling rate of 10 ℃/min and is kept for 2h, and then the soldered joint is heated to 0.7Ts =469 ℃ at the heating rate of 10 ℃/min and is kept for 2h.
(3) The joint is cooled to 0.4Ts =268 ℃ at a cooling rate of 10 ℃/min and is kept for 2h, and then is heated to 0.6Ts =401 ℃ at a heating rate of 10 ℃/min and is kept for 2h.
(4) Cooling the joint to 0.4Ts =268 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.5Ts =335 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
(5) Cooling the joint to 0.3Ts =201 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.4Ts =268 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
(6) Cooling the joint to 0.1Ts =67 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.3Ts =201 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
Then, as shown in fig. 5, the cryogenic cycle treatment is performed, the cycle number is 2, and the cryogenic cycle treatment specifically includes the following steps: the temperature of the soldered joint is reduced to-75 ℃ at the cooling rate of 10 ℃/min and is preserved for 2h, and then the temperature is increased to 0.3Ts =201 ℃ at the heating rate of 10 ℃/min and is preserved for 2h.
And finally, cooling the soldered joint to-75 ℃ at a cooling rate of 10 ℃/min, preserving the temperature for 2h, and then heating the soldered joint to room temperature at a heating rate of 10 ℃/min.
Example 2:
the only difference from example 1 is that the number of cycles of the treatment of the cryogenic cycle was 4.
Example 3:
the only difference from example 1 is that the cryogenic cycle treatment was not performed.
Example 4:
the only difference from example 1 is that the 316L stainless steel is loaded with a compressive stress parallel to the braze interface of 50MPa when brazed at 750 ℃.
Example 5:
s1, setting the expansion coefficient as alpha 1 =18×10 -6 /. Degree.C.and elastic modulus E 1 316L stainless steel of =206GPa, the expansion coefficient is alpha 2 =8×10 -6 /. Degree.C.and elastic modulus E 2 And (4) grinding and ultrasonically cleaning the alumina ceramic of which the density is 380GPa to remove surface oxide scales and impurities.
S2, adding an Ag71Cu26Ti3 brazing filler metal on a 316L stainless steel and alumina ceramic brazing interface at 860 ℃, preserving heat for 5min after the brazing filler metal is molten, and carrying out cooling and stress relief treatment on a brazed joint, wherein the solidus temperature of the Ag71Cu26Ti3 brazing filler metal used in the embodiment is Ts =773 ℃;
and carrying out cooling circulation treatment on the brazed joint after brazing connection, wherein the cooling circulation treatment specifically comprises the following steps:
(1) Cooling to 0.6Ts =464 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.8Ts =618 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
(2) And cooling the soldered joint to 0.5Ts =387 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.7Ts =541 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
(3) Cooling the joint to 0.4Ts =309 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.6Ts =464 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
(4) Cooling the joint to 0.4Ts =309 ℃ at a cooling rate of 10 ℃/min, and keeping the temperature for 2h, and then heating to 0.5Ts =387 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 2h.
(5) The joint is cooled to 0.3Ts =232 ℃ at a cooling rate of 10 ℃/min and is kept for 2h, and then is heated to 0.4Ts =309 ℃ at a heating rate of 10 ℃/min and is kept for 2h.
(6) The joint is cooled to 0.1Ts =77 ℃ at a cooling rate of 10 ℃/min and is kept for 2h, and then is heated to 0.3Ts =232 ℃ at a heating rate of 10 ℃/min and is kept for 2h.
Then, carrying out cryogenic circulating treatment, wherein the circulating frequency is 2, and the cryogenic circulating treatment specifically comprises the following steps: the temperature of the soldered joint is reduced to-75 ℃ at the cooling rate of 10 ℃/min and is kept for 2h, and then the temperature is increased to 0.3Ts =232 ℃ at the heating rate of 10 ℃/min and is kept for 2h.
And finally, cooling the brazing joint to-75 ℃ at a cooling rate of 10 ℃/min, preserving the temperature for 2h, and then heating the brazing joint to room temperature at a heating rate of 10 ℃/min.
Step S2, the brazing process is carried out under the condition that the vacuum degree is 10 -3 In a vacuum furnace under MPa.
Example 6:
the only difference from example 5 is that the 316L stainless steel is loaded with a compressive stress of 50MPa parallel to the brazing interface when brazed at 860 c.
Example 7:
the only difference from example 1 is that the brazing interface is provided with grooves as shown in fig. 6, wherein 1, YG20 cemented carbide, 200, 316L stainless steel, 3, grooves.
The groove is generally arranged on the base metal with larger volume, is suitable for being used in the preparation of large-scale soldered joints, can fully release stress, improves the performance of the soldered joints and prolongs the service life.
Comparative example 1:
the difference from the example 1 is only that the soldered joint after soldering connection is directly cooled to 0.3Ts =201 ℃ at a cooling rate of 10 ℃/min and is kept at the temperature for 2h without performing the circulating cooling treatment and the cryogenic circulating treatment.
Comparative example 2:
the only difference from example 5 is that, without performing the circulation cooling treatment and the cryogenic circulation treatment, the soldered joint after the soldering connection was directly cooled to room temperature at a cooling rate of 10 ℃/min.
Table 1: residual stress results of brazed joints prepared in examples 1 to 6 and comparative examples 1 to 2
| Examples | First base material | Second base material | Residual stress/MPa |
| Example 1 | 316L stainless steel | YG20 hard alloy | 35 |
| Example 2 | 316L stainless steel | YG20 hard alloy | 33 |
| Example 3 | 316L stainless steel | YG20 hard alloy | 46 |
| Example 4 | 316L stainless steel | YG20 hard alloy | 32 |
| Example 5 | 316L stainless steel | Alumina ceramics | 46 |
| Example 6 | 316L stainless steel | Alumina ceramics | 42 |
| Comparative example 1 | 316L stainless steel | YG20 hard alloy | 134 |
| Comparative example 2 | 316L stainless steel | Alumina ceramics | Cracking of ceramics |
FIG. 1 is an electron microscope image of the brazing interface of a 316L stainless steel and alumina ceramic brazing sample of example 5; in the figure, 100, alumina ceramics, 200, 316L stainless steel, 300, ag71Cu26Ti3 brazing filler metal. As can be seen from the figure, the brazed joint subjected to the cooling cycle treatment and the cryogenic cycle treatment has a complete interface and no cracks, which shows that the residual stress is extremely small, and almost has no obvious influence on the strength and the stress fracture resistance of the joint.
FIG. 2 is a macroscopic picture and an electron microscope picture of the surface of the alumina ceramic of the 316L stainless steel and alumina ceramic brazing sample in comparative example 2; FIG. 3 is an electron microscope image of the brazing interface of 316L stainless steel and alumina ceramic brazing sample in comparative example 2 under different magnifications; in the figure, 100, alumina ceramics, 200, 316L stainless steel, 300, ag71Cu26Ti3 brazing filler metal. As is clear from the figure, cracks were generated in the brazed joint not subjected to the circulation cooling treatment and the deep cooling circulation treatment, both in the surface and in the interior of the ceramic, indicating that the residual stress exceeded the fracture strength of the alumina ceramic base material.
As described above, the present invention eliminates the movable dislocations in the structure by the uneven deformation caused by the expansion/contraction effect of heat by the cooling cycle treatment and the deep cooling cycle treatment, entangles and increases the fixed dislocations, and reduces the residual stress in the structure of the soldered joint.
The technical scope of the invention claimed by the embodiments of the present application is not exhaustive, and new technical solutions formed by equivalent replacement of single or multiple technical features in the technical solutions of the embodiments are also within the scope of the invention claimed by the present application; in all the embodiments of the present invention, which are listed or not listed, each parameter in the same embodiment only represents an example (i.e., a feasible embodiment) of the technical solution, and there is no strict matching and limiting relationship between the parameters, wherein the parameters may be replaced with each other without departing from the axiom and the requirements of the present invention, unless otherwise specified.
The technical means disclosed by the scheme of the invention are not limited to the technical means disclosed by the technical means, and the technical scheme also comprises the technical scheme formed by any combination of the technical characteristics. While the foregoing is directed to embodiments of the present invention, it will be appreciated by those skilled in the art that various changes may be made in the embodiments without departing from the principles of the invention, and that such changes and modifications are intended to be included within the scope of the invention.
The specific embodiments described herein are merely illustrative of the spirit of the invention. Various modifications or additions may be made to the described embodiments or alternatives may be employed by those skilled in the art without departing from the spirit or ambit of the invention as defined in the appended claims.
Claims (9)
1. A method for reducing residual stress of a heterogeneous brazed joint, the method comprises brazing, and the brazing comprises heating, heat preservation and cooling circulation treatment, and is characterized in that the cooling circulation treatment comprises the following steps: at least 2 cycles of cooling, heat preservation, heating and heat preservation are carried out, the temperature after cooling is not higher than the temperature after cooling in the previous cooling cycle, and the temperature after heating is not higher than the temperature after heating in the previous cooling cycle;
the brazing specifically comprises the step of brazing and connecting a first base material and a second base material by using brazing filler metal, wherein the brazing connection meets the following calculation formula:
in which α is 1 Is the first base material expansion coefficient, T is the soldering joint soldering temperature, sigma 1 To apply stresses parallel to the brazing interface of the first base material, E 1 Is the first parent material elastic modulus, alpha 2 Is the second parent material expansion coefficient, sigma 2 To apply stress parallel to the brazing interface of the second base material, E 2 The second base material elastic modulus, t is room temperature.
2. The method for reducing the residual stress of the heterogeneous soldered joint according to claim 1, wherein in the cooling cycle treatment process, the temperature after cooling in the first cooling cycle is (0.5 to 0.7) Ts, the temperature after heating is (0.7 to 0.9) Ts, the temperature after cooling in the last cooling cycle is (0.1 to 0.2) Ts, the temperature after heating is (0.15 to 0.3) Ts, and Ts is the solidus temperature of the solder.
3. The method for reducing the residual stress of the heterogeneous soldered joint according to claim 2, wherein in the cooling cycle treatment process, the temperature after cooling in the first cooling cycle is (0.6-0.7) Ts, the temperature after heating is (0.8-0.9) Ts, the temperature after cooling in the last cooling cycle is (0.1-0.2) Ts, and the temperature after heating is (0.2-0.3) Ts.
4. The method for reducing the residual stress of the dissimilar brazed joint according to claim 1, wherein the cooling cycle treatment is followed by a cryogenic cycle treatment, the cryogenic cycle treatment comprises at least 2 cycles of cooling, heat preservation, heating and heat preservation, and the temperature after cooling in the cryogenic cycle treatment is T 1 The temperature after temperature rise is T 2 ，T 1 The range is (75 to 150) DEG C, T 2 The range is (0.2 to 0.3) Ts, and the temperature is reduced to T in the last cycle 1 And then preserving heat, heating to room temperature or cooling to room temperature after the last circulation is finished, wherein Ts is the solidus temperature of the brazing filler metal.
5. The method of reducing residual stress of a heterogeneous brazed joint according to claim 1, wherein the brazed joint satisfies the following calculation formula:
。
6. the method of reducing residual stress at a heterogeneous brazed joint of claim 1, wherein the solder comprises at least one of nickel-based, copper-based, silver-based, aluminum-based, zinc-based, and tin-based solders.
7. The method of reducing residual stress of a heterogeneous brazed joint according to claim 1, wherein the first parent material comprises at least one of carbon steel, alloy steel, aluminum alloy, copper alloy.
8. The method of reducing residual stress of a heterogeneous brazed joint according to claim 1, wherein the second parent material comprises at least one of cemented carbide, ceramic, carbon steel, alloy steel, copper alloy.
9. The method of reducing residual stress of a heterogeneous brazed joint according to claim 1, wherein the first parent material or the second parent material weld face comprises at least one of a groove and a hole.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210780917.2A CN114833410B (en) | 2022-07-05 | 2022-07-05 | Method for reducing residual stress of heterogeneous brazed joint |
| PCT/CN2022/119836 WO2024007453A1 (en) | 2022-07-05 | 2022-09-20 | Method for reducing residual stress of heterogeneous brazed joint |
| JP2022193097A JP7381699B1 (en) | 2022-07-05 | 2022-12-01 | Method for reducing residual stress in dissimilar solder joints |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210780917.2A CN114833410B (en) | 2022-07-05 | 2022-07-05 | Method for reducing residual stress of heterogeneous brazed joint |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114833410A CN114833410A (en) | 2022-08-02 |
| CN114833410B true CN114833410B (en) | 2022-10-14 |
Family
ID=82575222
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210780917.2A Active CN114833410B (en) | 2022-07-05 | 2022-07-05 | Method for reducing residual stress of heterogeneous brazed joint |
Country Status (3)
| Country | Link |
|---|---|
| JP (1) | JP7381699B1 (en) |
| CN (1) | CN114833410B (en) |
| WO (1) | WO2024007453A1 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114833410B (en) * | 2022-07-05 | 2022-10-14 | 中机智能装备创新研究院(宁波)有限公司 | Method for reducing residual stress of heterogeneous brazed joint |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4386727A (en) * | 1980-05-23 | 1983-06-07 | Unde Madhav A | Prevention of build up of residual stresses in welds during welding and subsequent reheat cycles |
| JPH10156523A (en) * | 1996-12-02 | 1998-06-16 | Mitsubishi Heavy Ind Ltd | Joining method of dissimilar material |
| CN102873447A (en) * | 2012-10-12 | 2013-01-16 | 天津冶金集团中兴盛达钢业有限公司 | Steel wire connecting method |
| KR101367865B1 (en) * | 2013-05-29 | 2014-02-27 | 국방과학연구소 | Brazing method between titanium alloy and stainless steel |
| CN107363358A (en) * | 2017-07-20 | 2017-11-21 | 吉林大学 | A kind of method for improving neodymium iron boron and steel or neodymium iron boron and neodymium iron boron soldering joint strength |
| CN112164660A (en) * | 2020-09-07 | 2021-01-01 | 中国电子科技集团公司第十四研究所 | Method for rapidly checking thermal mismatch stress of T/R assembly substrate and packaging material |
| CN112620851A (en) * | 2020-12-24 | 2021-04-09 | 湘潭大学 | Method for connecting graphite and stainless steel through high-temperature brazing of composite gradient interlayer |
| CN114178640A (en) * | 2021-09-24 | 2022-03-15 | 中国航发北京航空材料研究院 | Thermal shock-resistant graphite and metal brazing method |
| CN114395668A (en) * | 2020-12-07 | 2022-04-26 | 山西柴油机工业有限责任公司 | Critical solid solution and critical multiple cooling and temperature varying aging and annealing composite heat treatment method |
| CN114672631A (en) * | 2022-03-25 | 2022-06-28 | 中国石油大学(华东) | Method for regulating and controlling full-thickness structure-stress-performance uniformity of ultra-thick forging of large hydrogenation reactor |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6027472A (en) * | 1983-07-22 | 1985-02-12 | Isao Shoda | Heating method in brazing of sintered hard chip |
| JPH0659575B2 (en) * | 1985-11-27 | 1994-08-10 | 住友セメント株式会社 | Method of joining metal and ceramics |
| JP2861357B2 (en) * | 1990-10-17 | 1999-02-24 | 株式会社村田製作所 | Aluminum nitride-copper bonding method |
| JP3511860B2 (en) * | 1997-09-10 | 2004-03-29 | 株式会社日立製作所 | Crack repair method |
| GB2429892B (en) * | 2004-05-27 | 2008-05-21 | Kyocera Corp | Ceramic heater,and oxygen sensor and hair iron using the ceramic heater |
| US7276824B2 (en) * | 2005-08-19 | 2007-10-02 | U.I.T., L.L.C. | Oscillating system and tool for ultrasonic impact treatment |
| JP5248242B2 (en) * | 2008-08-28 | 2013-07-31 | 日本発條株式会社 | Dissimilar material joined body manufacturing method and dissimilar material joined body |
| CN104084658B (en) * | 2014-07-01 | 2017-04-12 | 北京工业大学 | Diffusion brazing connecting method for contact reaction of magnesium alloy and steel |
| CN106914673B (en) * | 2017-04-13 | 2018-07-17 | 中国石油大学(华东) | A kind of nickel-base material soldered fitting ingredient and mechanical property homogenization method |
| CN108672965B (en) * | 2018-05-07 | 2020-08-28 | 中国工程物理研究院电子工程研究所 | Method for relieving residual stress of ceramic and metal soldered joint |
| CN114833410B (en) * | 2022-07-05 | 2022-10-14 | 中机智能装备创新研究院(宁波)有限公司 | Method for reducing residual stress of heterogeneous brazed joint |
-
2022
- 2022-07-05 CN CN202210780917.2A patent/CN114833410B/en active Active
- 2022-09-20 WO PCT/CN2022/119836 patent/WO2024007453A1/en unknown
- 2022-12-01 JP JP2022193097A patent/JP7381699B1/en active Active
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4386727A (en) * | 1980-05-23 | 1983-06-07 | Unde Madhav A | Prevention of build up of residual stresses in welds during welding and subsequent reheat cycles |
| JPH10156523A (en) * | 1996-12-02 | 1998-06-16 | Mitsubishi Heavy Ind Ltd | Joining method of dissimilar material |
| CN102873447A (en) * | 2012-10-12 | 2013-01-16 | 天津冶金集团中兴盛达钢业有限公司 | Steel wire connecting method |
| KR101367865B1 (en) * | 2013-05-29 | 2014-02-27 | 국방과학연구소 | Brazing method between titanium alloy and stainless steel |
| CN107363358A (en) * | 2017-07-20 | 2017-11-21 | 吉林大学 | A kind of method for improving neodymium iron boron and steel or neodymium iron boron and neodymium iron boron soldering joint strength |
| CN112164660A (en) * | 2020-09-07 | 2021-01-01 | 中国电子科技集团公司第十四研究所 | Method for rapidly checking thermal mismatch stress of T/R assembly substrate and packaging material |
| CN114395668A (en) * | 2020-12-07 | 2022-04-26 | 山西柴油机工业有限责任公司 | Critical solid solution and critical multiple cooling and temperature varying aging and annealing composite heat treatment method |
| CN112620851A (en) * | 2020-12-24 | 2021-04-09 | 湘潭大学 | Method for connecting graphite and stainless steel through high-temperature brazing of composite gradient interlayer |
| CN114178640A (en) * | 2021-09-24 | 2022-03-15 | 中国航发北京航空材料研究院 | Thermal shock-resistant graphite and metal brazing method |
| CN114672631A (en) * | 2022-03-25 | 2022-06-28 | 中国石油大学(华东) | Method for regulating and controlling full-thickness structure-stress-performance uniformity of ultra-thick forging of large hydrogenation reactor |
Non-Patent Citations (1)
| Title |
|---|
| 陶瓷/金属钎焊接头强度研究现状;吴铭方等;《焊接技术》;20060825(第04期);第4-5页 * |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2024007308A (en) | 2024-01-18 |
| JP7381699B1 (en) | 2023-11-15 |
| CN114833410A (en) | 2022-08-02 |
| WO2024007453A1 (en) | 2024-01-11 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US9566655B2 (en) | Impeller brazing method | |
| CN112775431B (en) | Laser additive manufacturing method of titanium alloy/stainless steel dissimilar metal member | |
| JP2006291344A (en) | Ni-based alloy member, manufacturing method therefor, turbine engine part, welding material and manufacturing method therefor | |
| CN114833410B (en) | Method for reducing residual stress of heterogeneous brazed joint | |
| CN111468563A (en) | Correction method of titanium-tungsten square target assembly | |
| CN113478040B (en) | Active brazing method for improving performance of graphite/copper dissimilar material joint | |
| JP2017075382A (en) | Oxygen free copper plate, manufacturing method of oxygen free copper plate and ceramic wiring board | |
| CN111560611A (en) | Method for preparing transition layer of nickel-based coating on titanium alloy surface by laser cladding | |
| EP2853339B1 (en) | Welding material for welding of superalloys | |
| CN1846915A (en) | Double-metal hand saw blade and its production process | |
| CN113020735B (en) | Preparation method of silicon nitride ceramic/stainless steel braze welding joint with corrosion resistance and stress relief | |
| CN113478063B (en) | Titanium-zirconium-molybdenum alloy vacuum diffusion bonding method taking refractory metal as intermediate layer | |
| CN113070543B (en) | Method for brazing carbon material and nickel-based alloy by adopting Ag-Cr composite brazing filler metal | |
| CN113681103B (en) | Multi-brazing and heat treatment process for maintaining strength of nickel-based high-temperature alloy | |
| JPS60166165A (en) | Joining method of metal and ceramics | |
| CN110900037B (en) | Brazing filler metal and method for welding molybdenum-rhenium alloy and steel | |
| TW200927346A (en) | A diffusion bonding method for blocks of based bulk metallic glass | |
| CN114799395B (en) | Vacuum brazing method for dissimilar nickel-based high-temperature alloy for improving strength stability of joint | |
| CN114260614A (en) | Ti-Cr brazing filler metal of TZM alloy/graphite and brazing process thereof | |
| CN112872652B (en) | Ni-based superalloy welding wire with high Al, ti and Ta contents and preparation method and application thereof | |
| CN115338494B (en) | Method for regulating residual stress of heterogeneous brazed joint | |
| JP2002248597A (en) | High thermal conductive composite material and metallic mold | |
| CN113351884B (en) | Method for connecting CuCrZr/W dissimilar mutual non-solid-solution alloys based on laser additive manufacturing technology | |
| JPS6256378A (en) | Silicon carbide-metal bonded structure | |
| JPS6250073A (en) | Joined graphite-metal structural body |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| CP01 | Change in the name or title of a patent holder |
Address after: 315709 No. 929 Binhai Avenue, Danxi street, Xiangshan County, Ningbo City, Zhejiang Province (main building) 2002 Patentee after: Ningbo Intelligent Machine Tool Research Institute Co., Ltd. of China National Machinery Institute Group Patentee after: ZHENGZHOU RESEARCH INSTITUTE OF MECHANICAL ENGINEERING Co.,Ltd. Address before: 315709 No. 929 Binhai Avenue, Danxi street, Xiangshan County, Ningbo City, Zhejiang Province (main building) 2002 Patentee before: China Machinery Intelligent Equipment Innovation Research Institute (Ningbo) Co.,Ltd. Patentee before: ZHENGZHOU RESEARCH INSTITUTE OF MECHANICAL ENGINEERING Co.,Ltd. |
|
| CP01 | Change in the name or title of a patent holder | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20231229 Address after: 100000 No. 9, Wangzuo North Road, Yungang East, Fengtai District, Beijing Patentee after: Beijing Xinghang Electro-mechanical Equipment Co.,Ltd. Patentee after: ZHENGZHOU RESEARCH INSTITUTE OF MECHANICAL ENGINEERING Co.,Ltd. Address before: 315709 No. 929 Binhai Avenue, Danxi street, Xiangshan County, Ningbo City, Zhejiang Province (main building) 2002 Patentee before: Ningbo Intelligent Machine Tool Research Institute Co., Ltd. of China National Machinery Institute Group Patentee before: ZHENGZHOU RESEARCH INSTITUTE OF MECHANICAL ENGINEERING Co.,Ltd. |
|
| TR01 | Transfer of patent right |