CN117817185A - Nickel-based powder solder, preparation method thereof and application thereof in connection of homogeneous alloy or heterogeneous alloy - Google Patents
Nickel-based powder solder, preparation method thereof and application thereof in connection of homogeneous alloy or heterogeneous alloy Download PDFInfo
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- CN117817185A CN117817185A CN202310248080.1A CN202310248080A CN117817185A CN 117817185 A CN117817185 A CN 117817185A CN 202310248080 A CN202310248080 A CN 202310248080A CN 117817185 A CN117817185 A CN 117817185A
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- 239000000956 alloy Substances 0.000 title claims abstract description 133
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 126
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 87
- 239000000843 powder Substances 0.000 title claims abstract description 66
- 229910000679 solder Inorganic materials 0.000 title claims abstract description 48
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 37
- 238000002360 preparation method Methods 0.000 title abstract description 11
- 238000005219 brazing Methods 0.000 claims abstract description 95
- 239000002184 metal Substances 0.000 claims abstract description 37
- 229910052751 metal Inorganic materials 0.000 claims abstract description 37
- 239000000945 filler Substances 0.000 claims abstract description 36
- 238000000034 method Methods 0.000 claims abstract description 32
- 239000000126 substance Substances 0.000 claims abstract description 16
- 239000000463 material Substances 0.000 claims abstract description 15
- 238000009689 gas atomisation Methods 0.000 claims abstract description 11
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 230000008569 process Effects 0.000 claims description 17
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 229910000601 superalloy Inorganic materials 0.000 claims description 14
- 238000005507 spraying Methods 0.000 claims description 9
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 239000011230 binding agent Substances 0.000 claims description 7
- 238000007873 sieving Methods 0.000 claims description 7
- 239000010941 cobalt Substances 0.000 claims description 4
- 229910017052 cobalt Inorganic materials 0.000 claims description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 4
- 239000007789 gas Substances 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 2
- 238000004321 preservation Methods 0.000 claims description 2
- 239000000203 mixture Substances 0.000 abstract description 6
- 238000002844 melting Methods 0.000 description 24
- 239000007788 liquid Substances 0.000 description 18
- 238000001816 cooling Methods 0.000 description 17
- 230000008018 melting Effects 0.000 description 15
- 239000011159 matrix material Substances 0.000 description 14
- 239000010953 base metal Substances 0.000 description 12
- 230000005496 eutectics Effects 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 11
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 10
- 238000003466 welding Methods 0.000 description 10
- 230000007547 defect Effects 0.000 description 9
- 239000006104 solid solution Substances 0.000 description 9
- 238000002156 mixing Methods 0.000 description 6
- 244000137852 Petrea volubilis Species 0.000 description 5
- 238000004140 cleaning Methods 0.000 description 5
- 238000007599 discharging Methods 0.000 description 5
- 238000005304 joining Methods 0.000 description 5
- 238000010309 melting process Methods 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- 238000005498 polishing Methods 0.000 description 5
- 239000002994 raw material Substances 0.000 description 5
- 238000007711 solidification Methods 0.000 description 5
- 230000008023 solidification Effects 0.000 description 5
- 238000009792 diffusion process Methods 0.000 description 4
- 239000007791 liquid phase Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910000599 Cr alloy Inorganic materials 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910021332 silicide Inorganic materials 0.000 description 2
- FVBUAEGBCNSCDD-UHFFFAOYSA-N silicide(4-) Chemical compound [Si-4] FVBUAEGBCNSCDD-UHFFFAOYSA-N 0.000 description 2
- 238000005476 soldering Methods 0.000 description 2
- 241001062472 Stokellia anisodon Species 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 238000005495 investment casting Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 229910021334 nickel silicide Inorganic materials 0.000 description 1
- RUFLMLWJRZAWLJ-UHFFFAOYSA-N nickel silicide Chemical compound [Ni]=[Si]=[Ni] RUFLMLWJRZAWLJ-UHFFFAOYSA-N 0.000 description 1
- 239000012071 phase Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000009772 tissue formation Effects 0.000 description 1
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- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
The invention discloses a nickel-based powder solder, a preparation method thereof and application thereof in connection of a homogeneous alloy or a heterogeneous alloy, and belongs to the technical field of high-temperature brazing materials. The solder has the chemical composition (wt.%): 8.0 to 12.0 percent of Co, 8.0 to 12.5 percent of Cr, 2.0 to 6.0 percent of W, 1.3 to 3.5 percent of Mo, 1.5 to 6.5 percent of Al, 0 to 4.0 percent of Si, 0.5 to 1.8 percent of B, 0 to 5.0 percent of Nb, 0 to 0.3 percent of C and the balance of Ni. The brazing filler metal is prepared by adopting a gas atomization method and is used for alloy brazing connection. The brazing temperature is 1200-1300 ℃ and the brazing time is 10-90 minutes. The invention solves the problem of temperature bearing property of the high-temperature alloy brazing connection joint and the problem of high-performance connection between the high-temperature alloy and the wear-resistant alloy, and has important application value for connecting parts in high-temperature service environment.
Description
Technical Field
The invention relates to the technical field of high-temperature brazing materials, in particular to a nickel-based powder brazing filler metal, a preparation method thereof and application thereof in connection of a homogeneous alloy or a heterogeneous alloy.
Background
The high-temperature alloy is a high-alloy iron-based, nickel-based or cobalt-based austenitic metal material capable of working for a long time under the action of high temperature above 600 ℃ and certain stress, and has been widely applied to hot end parts of aeroengines and various industrial gas turbines from the moment of the prior art. However, because the turbine blade, the guide blade and other parts are designed to adopt complex internal cooling structures, the final structure is difficult to realize by precision casting technology alone, and high-performance connection of the superalloy blade and other superalloy components is required by a reliable brazing connection technology. In addition, the tip shroud contact surfaces of turbine blades are subject to severe wear, and there is also a need to braze the wear resistant alloy material to the tip shroud by reliable heterogeneous material braze joint techniques to reduce wear.
In recent years, due to the update of blade materials, the change of structures and the severe cracking condition of blade in service environments, blade cover plates and wear-resistant blocks frequently occur, the existing high-temperature brazing materials are difficult to meet the use requirements, so that the development of novel high-temperature brazing materials with excellent high-temperature performance, which are more suitable for high-temperature brazing, is urgently needed to solve the problems of high-performance brazing connection of high-temperature alloy materials and wear-resistant alloy materials.
Disclosure of Invention
The invention aims to provide a nickel-based powder solder, a preparation method thereof and application thereof in connection of a homogeneous alloy or a heterogeneous alloy, wherein the prepared powder solder is mainly applied to high-temperature brazing (1200-1300 ℃), can effectively solve the problem of connection of parts of the homogeneous (homogeneous high-temperature alloy) or heterogeneous alloy (high-temperature alloy and wear-resistant alloy) working in a severe environment, and has important application value.
In order to achieve the above purpose, the technical scheme of the invention is as follows:
a nickel-based powder braze, the braze being a nickel-based alloy powder; the brazing filler metal comprises the following chemical components in percentage by weight: 8.0 to 12.0 percent of Co, 8.0 to 12.5 percent of Cr, 2.0 to 6.0 percent of W, 1.3 to 3.5 percent of Mo, 1.5 to 6.5 percent of Al, 0 to 4.0 percent of Si, 0.5 to 1.8 percent of B, 0 to 5.0 percent of Nb, 0 to 0.3 percent of C and the balance of Ni; wherein: the powder brazing filler metal is spherical or nearly spherical, and the granularity is not more than 100 meshes.
The preparation process of the powder brazing filler metal comprises the following steps:
(1) According to the ingredients of the brazing filler metal, a vacuum induction furnace is adopted to smelt a mother alloy ingot of the brazing filler metal, and the smelting process comprises the following steps: preserving heat for 1-5 min at 1450-1570deg.C, pouring at 1390-1490 deg.C.
(2) Preparing master alloy ingots into alloy powder by a gas atomization method, wherein the technological parameters of the gas atomization method are as follows: the powder spraying temperature is 1400-1550 ℃, the mass flow rate is 2-6 kg/min, the powder spraying gas is argon, and the powder spraying pressure is 3-10 MPa;
(3) And sieving the prepared alloy powder to obtain the alloy powder with the mesh size not larger than 100, thus obtaining the powder solder.
The powder brazing alloy is applied to brazing connection of a homogeneous alloy or a heterogeneous alloy, wherein the homogeneous alloy refers to a homogeneous high-temperature alloy, and the heterogeneous alloy refers to a high-temperature alloy material and a wear-resistant alloy; such as Ni 3 Al-based wear-resistant alloy; co-Cr-Mo, co-Cr-W, co-Nb-Cr and other cobalt-based wear-resistant alloys; WC wear-resistant alloy.
In the brazing connection process, the brazing alloy powder is prepared into paste by utilizing an aqueous or oily binder and then is applied to a part to be welded of a sample, the sample is placed in a vacuum brazing furnace for brazing connection, and the brazing heat preservation time is 10-90 minutes. The tensile strength of the high-temperature alloy braze joint is not lower than 600MPa at 980 ℃; the tensile strength of the high-temperature alloy and wear-resistant alloy braze joint is not lower than 200MPa at 980 ℃.
The design concept and principle of the invention are as follows:
the traditional superalloy brazing is easy to form a large amount of nickel silicide and M after solidification of residual liquid phase of a welding seam in the postweld cooling process 23 B 6 And M 5 B 3 And the boride and other low-melting point eutectic structures, holes, cracks and other welding defects. These low melting point structure and weld defects become weak links affecting the reliability of the joint under the increasingly higher joint use temperature and performance requirements, especially when the dissimilar alloy base materials with different thermal expansion coefficients are brazed.
In order to solve the problems, the invention adoptsNickel is used as a matrix, and various alloy elements are added to regulate and control the structure. In the brazing cooling process, high-melting-point elements such as W, mo and the like which are derived from the diffusion of the brazing filler metal and the base metal are firstly separated out from Cr element and combined with B element to form M with stable structure 3 B 2 The boride with high melting point continuously grows, and the reaction process is 2B+W+Mo+Cr- & gt (Cr, W, mo) 3 B 2 This process is also a rapid consumption of the fuse element B and an improvement in the overall heat-carrying capacity of the weld. The invention regulates and controls the tissue formation at this stage through the coordination of elements and processes: the high melting point elements such as W, mo added by the brazing filler metal are matched with a higher brazing temperature to accelerate the diffusion of refractory elements in the base metal to the brazing filler metal and the diffusion of B elements in the brazing filler metal to the base metal, so that the liquid brazing filler metal obtains higher concentration of the refractory elements, and a large amount of B elements are consumed by diffusion and reaction at the stage to promote the melting point of a welding line and inhibit the formation of a low melting point eutectic structure at the next stage. With the continuous solidification, the components of the residual liquid solder are obviously changed, refractory elements are greatly consumed, and the residual liquid phase with a lower melting point gradually forms eutectic structures such as boride, silicide and the like with a low melting point in the subsequent solidification process. In order to avoid the formation of low-melting point eutectic structures which are unfavorable for the high-temperature performance of the joint, the Si content in the brazing filler metal is moderate, si can be dissolved in a weld joint matrix in a solid solution mode in the later cooling period without forming silicide, but the solubility of B element in matrix Ni is very low, if more B element and boride forming element still exist in liquid phase in the later cooling period, a large amount of low-melting point boride is difficult to avoid even if the cooling speed is increased, and the joint is more easily cracked due to the faster cooling speed, especially when heterogeneous materials are connected. The brazing filler metal in the invention is M 3 B 2 The growth stage of the phase basically eliminates B element, so that the occurrence of a low-melting point eutectic structure is avoided from the source, cr element is also greatly consumed in the initial solidification stage, and the residual Cr element, co, mo, al, nb and other elements continue to form a weld joint matrix with Ni element. The final weld joint matrix has the concentration of Cr, co and other elements close to that of the base metal, and has the functions of solid solution strengthening the weld joint and coordinating the weld joint metal and the base metal, and the Al, nb and other elements in the weld joint are strong through precipitationThe chemical action improves the high temperature performance of the joint. When materials with larger difference of thermal physical properties are brazed, the plasticity, the composition and the structural coordination of the welding seam are also particularly important, and the Co element which is similar to the content of the base metal matrix is added into the brazing filler metal, so that the Ti element which is easy to cause stress concentration is not added, and the welding seam cracking risk is reduced while the strength and the wear resistance are improved.
In conclusion, aiming at the higher and higher use temperature and performance requirements of the high-temperature alloy joint and the wear-resistant alloy joint, the invention adjusts and controls the weld joint structure by means of the element interaction of the liquid brazing filler metal and the base metal alloy in the brazing solidification process by blending the alloy element proportion, and eliminates the low-melting point eutectic, thereby greatly improving the temperature bearing capacity of the joint.
The beneficial effects of the invention are as follows:
by adopting the brazing material and the brazing process, the matrix of the obtained brazing joint is nickel-based austenite, a large amount of alloy elements are dissolved in the matrix in a solid solution way, part of alloy elements are precipitated in the matrix in the form of boride with stable high melting point, and the joint is mainly strengthened in a solid solution strengthening way and a precipitation strengthening way. The brazing filler metal has good fluidity, less corrosion to a base material and higher high-temperature mechanical property than the traditional brazing joint, and compared with the traditional brazing material, the brazing material provided by the invention is suitable for brazing the same high-temperature alloy material, is also suitable for brazing the high-temperature alloy and the wear-resistant alloy material, and has a wider application range.
Drawings
FIG. 1 is an appearance of a nickel-based alloy powder braze.
FIG. 2 is a DTA curve of the solder powder in example 1.
FIG. 3 is a microstructure of a joint made by brazing DD419 alloy with nickel-based filler metal in example 1.
FIG. 4 is a graph of joint tensile strength of DD419 alloy brazed with nickel-based filler metal in example 1.
FIG. 5 is a joint microstructure of example 2 brazing DD419 alloy with nickel-based filler metal.
FIG. 6 is a graph of joint tensile strength of DD419 alloy brazed with nickel-based filler metal in example 2.
FIG. 7 shows the microstructure of a joint made by brazing DD426 with a Co-Nb-Cr alloy using a nickel-based filler metal in example 3.
FIG. 8 is a graph of joint tensile strength of DD426 and Co-Nb-Cr alloys brazed using nickel-based braze in example 3.
FIG. 9 is a microstructure of a joint of comparative example 1 in which the DD419 alloy was brazed with a nickel-based filler metal.
FIG. 10 is a graph of joint tensile strength of comparative example 1 using nickel-based filler metal to braze the DD419 alloy.
FIG. 11 is a microstructure of a joint of comparative example 2 where DD5 and MX25B alloys were brazed using a nickel-based powder braze.
FIG. 12 is a graph of joint tensile strength of comparative example 2 braze-welded DD5 and MX25B alloys using nickel-based powder braze.
Detailed Description
The invention is described in detail below with reference to the drawings and examples.
In the following examples, master alloy ingots were prepared into alloy powders by gas atomization, the process parameters of which were: the powder spraying temperature is 1480 ℃, the mass flow rate is 3.5kg/min, the powder spraying gas is argon, and the powder spraying pressure is 5.5MPa.
Example 1
The base metal to be welded in the embodiment is nickel-based superalloy DD419, and the alloy comprises the following chemical components in percentage by weight:
9.5% of Co, 6.3% of Cr, 6.5% of W, 6.6% of Ta, 5.5% of Al, 3.1% of Re, 0.9% of Ti, 0.5% of Mo and the balance of Ni.
The solder comprises the following chemical components in percentage by weight:
9% of Co, 12.4% of Cr, 4.5% of W, 3.4% of Mo, 6% of Al, 0.2% of Si, 0.8% of B, 0.04% of C and the balance of Ni.
The preparation method of the solder comprises the following steps: raw materials with purity more than 99.99 percent are proportionally prepared and then put into a vacuum arc melting furnace to be melted into alloy ingots, and the melting process comprises the following steps: preserving heat at 1550 ℃ for 3min to 1480 ℃ for casting; and preparing alloy powder from the smelted alloy ingot by a gas atomization method, namely remelting the master alloy ingot to form liquid flow, atomizing the liquid flow into fine liquid drops by using argon impact, rapidly cooling to form the alloy powder, and sieving the alloy powder with the particle size of not more than 100 meshes. The morphology of the prepared nickel-based powder solder is shown in figure 1, and the nickel-based powder solder is spherical or nearly spherical. The DTA curve of the powder braze in this example is shown in fig. 2.
Before welding, solid solution state nickel-base superalloy DD419 is processed intoPolishing the surface to be welded by using No. 800 sand paper, ultrasonically cleaning the surface to be welded for 15min in acetone to remove greasy dirt on the surface of the sample to be welded, blending solder powder into paste by using a nicrobraz's' binder, applying the paste to the part to be welded of the sample, smearing Nicrobraz White Stop Off Type II type solder resist on the area near the paste solder to prevent the solder from losing in the brazing process, placing the sample into a vacuum brazing furnace for brazing, wherein the brazing temperature is 1290 ℃, the brazing time is 90min, cooling to below 80 ℃, discharging, and performing effective treatment.
FIG. 3 is a microstructure of a sample braze joint, and it can be seen that the weld joint structure is dense, white boride is distributed in a matrix, and no defects and low-melting eutectic structure are found; figure 4 shows the tensile properties of a sample braze joint after joining at 980 c.
Example 2
The base metal to be welded in the embodiment is nickel-based superalloy DD419, and the alloy comprises the following chemical components in percentage by weight:
9.5% of Co, 6.3% of Cr, 6.5% of W, 6.6% of Ta, 5.5% of Al, 3.1% of Re, 0.9% of Ti, 0.5% of Mo and the balance of Ni.
The solder comprises the following chemical components in percentage by weight:
9% of Co, 9% of Cr, 4% of W, 3.2% of Mo, 4.2% of Al, 3.3% of Si, 1.2% of B, 1.5% of Nb, 0.15% of C and the balance of Ni.
The preparation method of the solder comprises the following steps: raw materials with purity more than 99.99 percent are proportionally prepared and then put into a vacuum arc melting furnace to be melted into alloy ingots, and the melting process comprises the following steps: preserving the temperature at 1540 ℃ for 3min and pouring at 1470 ℃; and preparing alloy powder from the smelted alloy ingot by a gas atomization method, namely remelting the master alloy ingot to form liquid flow, atomizing the liquid flow into fine liquid drops by using argon impact, rapidly cooling to form the alloy powder, and sieving the alloy powder with the particle size of not more than 100 meshes.
Before welding, solid solution cobalt-based superalloy DD419 is processed intoPolishing the surface to be welded by using No. 800 sand paper, ultrasonically cleaning the surface to be welded for 15min in acetone to remove greasy dirt on the surface of the sample to be welded, blending solder powder into paste by using a nicrobraz's' binder, applying the paste to the part to be welded of the sample, smearing Nicrobraz White Stop Off Type II type solder resist on the area near the paste solder to prevent the solder from losing in the brazing process, placing the sample into a vacuum brazing furnace for brazing, cooling the sample to below 80 ℃ for 25min at the brazing temperature, discharging the sample, and performing effective treatment.
FIG. 5 is a microstructure of a sample braze joint, and it can be seen that the weld joint structure is dense, white boride is distributed in a matrix, and no defects and low-melting eutectic structure are found; figure 6 shows the tensile properties of a sample braze joint after joining at 980 c.
Example 3
The base metal to be welded in the embodiment is nickel-based superalloy DD426 and a Co-Nb-Cr wear-resistant alloy.
The DD426 alloy has the following chemical composition (wt.%):
9% of Co, 5% of Cr, 12% of W, 6% of Al, 1.1% of Ti, 1.1% of Mo, 1.4% of Nb, 0.15% of C and the balance of Ni.
The chemical composition of the Co-Nb-Cr wear resistant alloy is as follows (wt.%):
26% of Nb, 19% of Cr and the balance of Co.
The solder comprises the following chemical components in percentage by weight:
9% of Co, 8.5% of Cr, 4% of W, 1.7% of Mo, 4.5% of Al, 1% of B, 3.7% of Nb, 0.16% of C and the balance of Ni.
The preparation method of the solder comprises the following steps: raw materials with purity more than 99.99 percent are proportionally prepared and then put into a vacuum arc melting furnace to be melted into alloy ingots, and the melting process comprises the following steps: preserving the temperature at 1540 ℃ for 3min and pouring at 1470 ℃; and preparing alloy powder from the smelted alloy ingot by a gas atomization method, namely remelting the master alloy ingot to form liquid flow, atomizing the liquid flow into fine liquid drops by using argon impact, rapidly cooling to form the alloy powder, and sieving the alloy powder with the particle size of not more than 100 meshes.
Before welding, solid solution DD426 and Co-Nb-Cr abrasion-resistant alloy are respectively processed intoPolishing the surface to be welded by using No. 800 sand paper, ultrasonically cleaning the surface to be welded for 15min in acetone to remove greasy dirt on the surface of the sample to be welded, blending solder powder into paste by using a nicrobraz's' binder, applying the paste to the part to be welded of the sample, smearing Nicrobraz White Stop Off Type II type solder resist on the area near the paste solder to prevent the solder from losing in the brazing process, placing the sample into a vacuum brazing furnace for brazing, cooling the sample to the temperature of below 80 ℃ for 12min, discharging the sample, and performing effective treatment.
FIG. 7 is a microstructure of a sample braze joint, co-Nb-Cr abrasion resistant alloy is arranged on the left side of a weld joint, DD426 alloy is arranged on the right side of the weld joint, and as can be seen, the weld joint has compact structure, white boride is distributed in a matrix, and no defect and low-melting point eutectic structure are found; figure 8 shows the tensile properties of a sample braze joint after joining at 980 c.
Comparative example 1
The base metal to be welded in the comparative example is nickel-based superalloy DD419, and the alloy comprises the following chemical components in percentage by weight:
9.5% of Co, 6.3% of Cr, 6.5% of W, 6.6% of Ta, 5.5% of Al, 3.1% of Re, 0.9% of Ti, 0.5% of Mo and the balance of Ni.
The solder comprises the following chemical components in percentage by weight:
8% of Co, 11% of Cr, 7% of W, 3% of Mo, 5% of Al, 0.2% of Si, 0.4% of B, 0.2% of Nb, 0.1% of C and the balance of Ni.
The preparation method of the solder comprises the following steps: raw materials with purity more than 99.99 percent are proportionally prepared and then put into a vacuum arc melting furnace to be melted into alloy ingots, and the melting process comprises the following steps: preserving heat at 1550 ℃ for 3min to 1480 ℃ for casting; and preparing alloy powder from the smelted alloy ingot by a gas atomization method, namely remelting the master alloy ingot to form liquid flow, atomizing the liquid flow into fine liquid drops by using argon impact, rapidly cooling to form the alloy powder, and sieving the alloy powder with the particle size of not more than 100 meshes.
Before welding, solid solution state nickel-base superalloy DD419 is processed intoPolishing the surface to be welded by using No. 800 sand paper, ultrasonically cleaning the surface to be welded for 15min in acetone to remove greasy dirt on the surface of the sample to be welded, blending solder powder into paste by using a nicrobraz's' binder, applying the paste to the part to be welded of the sample, smearing Nicrobraz White Stop Off Type II type solder resist on the area near the paste solder to prevent the solder from losing in the brazing process, placing the sample into a vacuum brazing furnace for brazing, wherein the brazing temperature is 1290 ℃, the brazing time is 60min, cooling to below 80 ℃, discharging, and performing effective treatment.
FIG. 9 is a microstructure of a sample braze joint, as can be seen, a plurality of hole defects appear in the weld; figure 10 shows the tensile properties of a sample braze joint after joining at 980 c.
Comparative example 2
The base metal to be welded in the comparative example is nickel-based superalloy DD405 and wear-resistant alloy MX25B.
The DD405 alloy has the following chemical composition (wt.%):
cr 7%, co 8%, W5%, al 6%, ta 6.3%, mo 1.7%, re 3%, hf 0.1%, and Ni in balance.
The chemical composition of MX25B alloy is (wt.%):
cr 5%, al 10%, ti 2%, W3%, and Ni in balance.
The solder comprises the following chemical components in percentage by weight:
11% of Co, 12% of Cr, 3.5% of W, 0.3% of Mo, 2% of Al, 5% of Si, 1.3% of B, 1% of Nb, 0.2% of C and the balance of Ni.
The preparation method of the solder comprises the following steps: raw materials with purity more than 99.99 percent are proportionally prepared and then put into a vacuum arc melting furnace to be melted into alloy ingots, and the melting process comprises the following steps: preserving heat at 1530 ℃ for 3min to 1450 ℃ and pouring; and preparing alloy powder from the smelted alloy ingot by a gas atomization method, namely remelting the master alloy ingot to form liquid flow, atomizing the liquid flow into fine liquid drops by using argon impact, rapidly cooling to form the alloy powder, and sieving the alloy powder with the particle size of not more than 100 meshes.
Before welding, solid solution state nickel-base superalloy DD405 and MX25B wear-resistant alloy are processed intoPolishing the surface to be welded by using No. 800 sand paper, ultrasonically cleaning the surface to be welded for 15min in acetone to remove greasy dirt on the surface of the sample to be welded, blending solder powder into paste by using a nicrobraz's' binder, applying the paste to the part to be welded of the sample, smearing Nicrobraz White Stop Off Type II type solder resist on the area near the paste solder to prevent the solder from losing in the brazing process, placing the sample into a vacuum brazing furnace for brazing, wherein the brazing temperature is 1180 ℃, the brazing time is 30min, cooling to below 80 ℃, discharging, and performing effective treatment.
FIG. 11 is a microstructure of a sample braze joint, showing the presence of multiple hole defects and a large number of low melting eutectic structures in the weld; figure 12 shows the tensile properties of a sample braze joint after joining at 980 c.
As can be seen from the microstructure diagrams of the sample braze joints in the above examples 1-3, the weld matrix structure is uniform and compact, no obvious weld defects and low-melting eutectic structure are seen, and part of refractory elements are precipitated in the form of boride in the weld matrix in a supersaturated state. As can be seen from the 980 ℃ tensile property test results of the samples after brazing connection in the above embodiments 1-3, the high-temperature strength of the joint after brazing connection is higher, the tensile strength of the high-temperature alloy brazing joint under 980 ℃ test condition is not lower than 600MPa, and the tensile strength of the high-temperature alloy and wear-resistant alloy brazing joint under 980 ℃ test condition is not lower than 200MPa, which shows that compared with the traditional brazing filler metal, the brazing filler metal is more suitable for high-performance connection of parts in a high-temperature service environment.
As can be seen from the microstructure of the sample braze of comparative examples 1-2, there are many more weld defects in the braze than in examples 1-3, where the braze of comparative example 2 also has a large amount of eutectic structures with low melting point, which all lead to reduced high temperature performance of the joint. As can be seen from the tensile property test results of the samples after connection in comparative examples 1-2, the tensile strength of the high-temperature alloy soldered joint is less than 600MPa under the test condition of 980 ℃, and the tensile strength of the high-temperature alloy and wear-resistant alloy soldered joint is less than 200MPa under the test condition of 980 ℃, which means that the tensile strength requirement of the joint cannot be met when the solder component exceeds the limit range of the solder component or the soldering temperature exceeds the specified soldering temperature range of the solder.
Claims (7)
1. A nickel-based powder solder, characterized in that: the brazing filler metal is nickel-based alloy powder; the brazing filler metal comprises the following chemical components in percentage by weight:
8.0 to 12.0 percent of Co, 8.0 to 12.5 percent of Cr, 2.0 to 6.0 percent of W, 1.3 to 3.5 percent of Mo, 1.5 to 6.5 percent of Al, 0 to 4.0 percent of Si, 0.5 to 1.8 percent of B, 0 to 5.0 percent of Nb, 0 to 0.3 percent of C and the balance of Ni.
2. The nickel-based powder filler metal of claim 1, wherein: the powder brazing filler metal is spherical or nearly spherical, and the granularity is not more than 100 meshes.
3. The method for preparing nickel-based powder solder according to claim 1, wherein: the method comprises the following steps:
(1) Preparing materials according to the components of the brazing filler metal, and smelting a mother alloy ingot of the brazing filler metal by adopting a vacuum induction furnace;
(2) Preparing master alloy ingots into alloy powder by a gas atomization method, wherein the technological parameters of the gas atomization method are as follows: the powder spraying temperature is 1400-1550 ℃, the mass flow rate is 2-6 kg/min, the powder spraying gas is argon, and the powder spraying pressure is 3-10 MPa;
(3) And sieving the prepared alloy powder to obtain the alloy powder with the mesh size not larger than 100, thus obtaining the powder solder.
4. The method for preparing the nickel-based powder solder for superalloy connection and wear-resistant alloy connection according to claim 3, wherein the method comprises the following steps: in the step (1), the smelting process is as follows: preserving heat for 1-5 min at 1450-1570deg.C, pouring at 1390-1490 deg.C.
5. Use of nickel-based filler metal in a homo-or hetero-alloy joint according to claim 1, characterized in that: the powder brazing filler metal is applied to brazing connection of the same high-temperature alloy material, and the brazing temperature is 1200-1300 ℃; alternatively, the powder braze is applied to superalloy materials and wear resistant alloys (e.g., ni 3 Al-based wear-resistant alloy; co-Cr-Mo, co-Cr-W, co-Nb-Cr and other cobalt-based wear-resistant alloys; WC wear resistant alloy) and the brazing temperature is 1200-1300 ℃.
6. Use of the nickel-based filler metal according to claim 5 in a homo-or hetero-alloy joint, characterized in that: in the brazing connection process, the brazing alloy powder is prepared into paste by utilizing an aqueous or oily binder and then is applied to a part to be welded of a sample, the sample is placed in a vacuum brazing furnace for brazing connection, and the brazing heat preservation time is 10-90 minutes.
7. Use of the nickel-based filler metal according to claim 6 in a homo-or hetero-alloy joint, characterized in that: after the brazing connection, the tensile strength of the high-temperature alloy brazing joint is not lower than 600MPa at 980 ℃; the tensile strength of the high-temperature alloy and wear-resistant alloy braze joint is not lower than 200MPa at 980 ℃.
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