Ni3Post-treatment method for Al-based single crystal alloy after welding
阅读说明：本技术 一种Ni3Al基单晶合金焊后的后处理方法 (Ni3Post-treatment method for Al-based single crystal alloy after welding ) 是由 宫声凯 梁资拓 曹阳 裴延玲 李树索 于 2021-09-07 设计创作，主要内容包括：本发明涉及焊后处理技术领域,尤其涉及一种Ni-(3)Al基单晶合金焊后的后处理方法。本发明提供的后处理方法,包括以下步骤：将焊后Ni-(3)Al基单晶合金进行热处理,得到Ni-(3)Al基单晶合金的焊接件；所述热处理的温度为1050～1100℃。根据实施例的记载,经过本发明所述的热处理进行处理后得到的Ni-(3)Al基单晶合金的焊接件在980℃时的抗拉强度在650MPa以上,基体抗拉强度在95％以上。且所述后处理方法简单,条件易控制,可适用于大规模的工业生产,具有显著的工业应用价值和经济效益。(The invention relates to the technical field of postweld treatment, in particular to Ni 3 A post-treatment method of Al-based single crystal alloy after welding. The post-processing method provided by the invention comprises the following steps: to weld Ni 3 Heat treating Al-base monocrystal alloy to obtain Ni 3 A weldment of an Al-based single crystal alloy; the temperature of the heat treatment is 1050-1100 ℃. According to the description of the examples, Ni obtained after treatment by the heat treatment according to the invention 3 Al-based sheetThe tensile strength of the welding piece of the crystal alloy is above 650MPa at 980 ℃, and the tensile strength of the matrix is above 95%. And the post-treatment method is simple, the conditions are easy to control, and the method is suitable for large-scale industrial production and has obvious industrial application value and economic benefit.)
1. Ni3The post-treatment method of the Al-based single crystal alloy after welding is characterized by comprising the following steps of:
to weld Ni3Heat treating Al-base monocrystal alloy to obtain Ni3A weldment of an Al-based single crystal alloy;
the temperature of the heat treatment is 1050-1100 ℃.
2. The post-treatment method according to claim 1, wherein the temperature of the heat treatment is 1060 to 1080 ℃.
3. The post-treatment method according to claim 1, wherein the heat treatment time is 8 to 12 hours.
4. The post-treatment method according to any one of claims 1 to 3, wherein the post-weld Ni is3The preparation method of the Al-based single crystal alloy comprises the following steps:
mixing Ni3Brazing Al-based single crystal alloy to obtain post-welded Ni3An Al-based single crystal alloy;
the brazing mode is vacuum brazing.
5. The post-treatment method according to claim 4, wherein the vacuum degree of the vacuum brazing is (5 to 7) x 10- 3Pa。
6. The post-processing method according to claim 5, wherein the vacuum brazing process comprises: heating from room temperature to 460-480 ℃ at a heating rate of 5-10 ℃/min, and keeping the temperature for 30-50 min; heating from 460-480 ℃ to 980-1000 ℃ at a heating rate of 5-10 ℃/min, and preserving heat for 10-50 min; heating from 980-1000 ℃ to 1200-1300 ℃ at a heating rate of 3-8 ℃/min, and preserving heat for 10-180 min.
7. The post-treatment method according to claim 4, wherein the Ni is subjected to brazing before the brazing3The Al-based single crystal alloy is pretreated.
8. The post-processing method according to claim 7, wherein the pre-processing comprises the steps of:
adding the Ni3After the end face of the Al-based single crystal alloy is ground flat, cleaning is carried out to obtain Ni with clean end face3An Al-based single crystal alloy;
two pieces of Ni with clean cross sections3And fixing an Al-based single crystal alloy butt joint tool, and coating brazing filler metal on a welding joint.
9. The post-processing method according to claim 8, wherein when the butt joint tool is fixed, two pieces of Ni with clean cross sections are adopted3The gap between the Al-based single crystal alloys is 10 to 200 μm.
10. The post-processing method according to claim 8 or 9, wherein the butt joint tool is fixed by spot welding with a platinum sheet.
Technical Field
The invention relates to the technical field of postweld treatment, in particular to Ni3A post-treatment method of Al-based single crystal alloy after welding.
Background
Ni3The Al-based single crystal alloy has the characteristics of very high-temperature strength, good creep deformation and fatigue resistance, excellent oxidation resistance and corrosion resistance, reliable tissue structure and the like, and is widely applied to turbine blades of aeroengines. But Ni3Since Al-based single crystal alloys have a high refractory element content and are likely to generate thermal cracks in the weld zone and the heat affected zone, resulting in poor weldability of high temperature alloys, vacuum brazing, Transient Liquid Phase (TLP) diffusion welding, or the like is generally used. Compared with TLP diffusion welding, the vacuum brazing has the advantages of low difficulty, convenient operation, good reliability and the like, and is widely applied to engineering.
The vacuum brazing method for the turbine blade of the aircraft engine is mainly applied to the following aspects: 1) welding the rafter of the high-pressure turbine guide blade, wherein the high-pressure turbine guide blade needs to be fixed between a turbine disc and a casing, so that the rafter needs to be welded at the top to facilitate the fixation of the guide blade; 2) the double or triple guide vanes are welded, and the turbine guide vanes are generally connected by adopting a brazing process to reduce aerodynamic loss and improve the turbine efficiency; 3) the blade repair and welding technology can also be used for repair and maintenance of turbine blades of aeroengines, and the abrasion, cracks and the like on the turbine blades and the working blades can be repaired by brazing, diffusion welding and the like.
Although the vacuum brazing method can effectively weld the turbine blade, the welded joint has the problems of non-uniform joint structure, more joint hard and brittle phases and large residual stress, so that the joint performance cannot always meet the use requirement. Aiming at the problems, a mechanical stretching mode is generally adopted at present to solve the problems, but the mechanical stretching method may generate mixed crystals, so that the mechanical property is poor, and the external stress condition is difficult to control.
Disclosure of Invention
The invention aims to provide Ni3A post-treatment method of Al-based single crystal alloy after welding. The post-treatment method can effectively improve the microstructure and the mechanical property of the welding joint.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides Ni3The post-welding treatment method of the Al-based single crystal alloy comprises the following steps:
to weld Ni3Heat treating Al-base monocrystal alloy to obtain Ni3A weldment of an Al-based single crystal alloy;
the temperature of the heat treatment is 1050-1100 ℃.
Preferably, the temperature of the heat treatment is 1060-1080 ℃.
Preferably, the time of the heat treatment is 8-12 h.
Preferably, the post-weld Ni3The preparation method of the Al-based single crystal alloy comprises the following steps:
mixing Ni3Brazing Al-based single crystal alloy to obtain post-welded Ni3An Al-based single crystal alloy;
the brazing mode is vacuum brazing.
Preferably, the vacuum degree of the vacuum brazing is (5-7) multiplied by 10-3Pa。
Preferably, the vacuum brazing process comprises: heating from room temperature to 460-480 ℃ at a heating rate of 5-10 ℃/min, and keeping the temperature for 30-50 min; heating from 460-480 ℃ to 980-1000 ℃ at a heating rate of 5-10 ℃/min, and preserving heat for 10-50 min; heating from 980-1000 ℃ to 1200-1300 ℃ at a heating rate of 3-8 ℃/min, and preserving heat for 10-180 min.
Preferably, the Ni is added before the brazing3The Al-based single crystal alloy is pretreated.
Preferably, the pretreatment comprises the following steps:
adding the Ni3After the end face of the Al-based single crystal alloy is ground flat, cleaning is carried out to obtain Ni with clean end face3Al-based sheetA crystalline alloy;
two pieces of Ni with clean cross sections3And fixing an Al-based single crystal alloy butt joint tool, and coating brazing filler metal on a welding joint.
Preferably, when the butt joint tool is fixed, the two pieces of Ni with clean cross sections3The gap between the Al-based single crystal alloys is 10 to 200 μm.
Preferably, the butt joint tool is fixed by spot welding through a platinum sheet.
The invention provides Ni3The post-welding treatment method of the Al-based single crystal alloy comprises the following steps: to weld Ni3Heat treating Al-base monocrystal alloy to obtain Ni3A weldment of an Al-based single crystal alloy; the temperature of the heat treatment is 1050-1100 ℃. The invention adopts the heat treatment temperature, which not only meets the requirement of rapid diffusion of elements in the welding seam, but also is lower than the heat treatment temperature of the matrix, thereby leading the joint structure to be more uniform, leading the isothermal solidification area to be wider and leading the joint performance to be better under the premise of less damage to the matrix. According to the description of the examples, Ni obtained after treatment by the heat treatment according to the invention3The tensile strength of a welded piece of the Al-based single crystal alloy is above 650MPa at 980 ℃, and the tensile strength of a matrix is above 95%. And the post-treatment method is simple, the conditions are easy to control, and the method is suitable for large-scale industrial production and has obvious industrial application value and economic benefit.
Drawings
FIG. 1 is a temperature control program curve of the vacuum brazing and heat treatment process of the present invention;
FIG. 2 shows Ni as described in example 13Metallographic structure of a weld joint of a weld part of the Al-based single crystal alloy;
FIG. 3 shows Ni as described in example 23The metallographic structure of a weld joint of a weld of the Al-based single crystal alloy.
Detailed Description
The invention provides Ni3The post-welding treatment method of the Al-based single crystal alloy comprises the following steps:
to weld Ni3Heat treating Al-base monocrystal alloy to obtainNi3A weldment of an Al-based single crystal alloy;
the temperature of the heat treatment is 1050-1100 ℃.
In the present invention, all the raw materials are commercially available products well known to those skilled in the art unless otherwise specified.
In the present invention, the post-weld Ni3The method for producing the Al-based single crystal alloy preferably includes: mixing Ni3Brazing Al-based single crystal alloy to obtain post-welded Ni3An Al-based single crystal alloy; the brazing mode is vacuum brazing.
In the invention, Ni3Brazing Al-based single crystal alloy to obtain post-welded Ni3An Al-based single crystal alloy.
Invention is directed to said Ni3The kind of the Al-based single crystal alloy is not particularly limited, and those known to those skilled in the art may be used. In a specific embodiment of the invention, the Ni3The Al-based single crystal alloy is specifically an IC21 alloy.
In the present invention, the Ni3The Al-based single crystal alloy is preferably Ni after heat treatment3An Al-based single crystal alloy; the heat treatment process is not particularly limited, and may be performed by a process known to those skilled in the art.
Before the brazing is carried out, the Ni is preferably treated by the invention3The Al-based single crystal alloy is pretreated. In the present invention, the pretreatment preferably includes the steps of:
adding the Ni3After the end face of the Al-based single crystal alloy is ground flat, cleaning is carried out to obtain Ni with clean end face3An Al-based single crystal alloy;
two pieces of Ni with clean cross sections3And fixing an Al-based single crystal alloy butt joint tool, and coating brazing filler metal on a welding joint.
The invention uses the Ni3After the end face of the Al-based single crystal alloy is ground flat, cleaning is carried out to obtain Ni with clean end face3An Al-based single crystal alloy.
Before the grinding is carried out, the invention preferably processes the Ni3The Al-based single crystal alloy is subjected to dicing treatment. The invention is to cut the blocksThe treatment is not particularly limited, and may be carried out by a procedure known to those skilled in the art. The process of the present invention is not particularly limited, and may be carried out by a process known to those skilled in the art.
In the invention, the cleaning solution used for cleaning is preferably acetone; the cleaning is preferably carried out under the condition of ultrasound; the time of the ultrasonic treatment is preferably 15 min; the present invention does not have any particular limitation on the frequency of the ultrasound, and may be performed using a frequency known to those skilled in the art.
Obtaining Ni with clean end face3After Al-based single crystal alloy, the invention makes two pieces of Ni with clean cross sections3And fixing an Al-based single crystal alloy butt joint tool, and coating brazing filler metal on a welding joint.
In the invention, when the butt joint tool is fixed, two pieces of Ni with clean sections3The gap between the Al-based single crystal alloys is preferably 10 to 200 μm, more preferably 50 to 100 μm, and most preferably 50 μm.
In the invention, the butt joint tool is preferably fixed by spot welding by adopting a platinum sheet; the process of spot welding is not particularly limited in the present invention, and may be performed by a process known to those skilled in the art.
In the present invention, the brazing filler metal preferably includes the following alloying elements in percentage by mass: 1-2 wt% of B, 1-3 wt% of Si, 6-8 wt% of Ti, 1-3 wt% of Al, 7-9 wt% of Co, 1-4 wt% of W, 8-11 wt% of Cr and the balance of Ni.
The coating process of the present invention is not particularly limited, and may be carried out by a process known to those skilled in the art.
In the invention, the brazing mode is preferably vacuum brazing; the vacuum degree of the vacuum brazing is preferably less than or equal to 7 x 10-3Pa, more preferably (5 to 7). times.10-3Pa, most preferably 7X 10-3Pa。
In the present invention, the vacuum brazing process preferably includes: heating from room temperature to 460-480 ℃ at a heating rate of 5-10 ℃/min, and keeping the temperature for 30-50 min; heating from 460-480 ℃ to 980-1000 ℃ at a heating rate of 5-10 ℃/min, and preserving heat for 10-50 min; heating from 980-1000 ℃ to 1200-1300 ℃ at a heating rate of 3-8 ℃/min, and preserving heat for 10-180 min. More preferably, the temperature is raised from room temperature to 465-475 ℃ at the temperature raising rate of 8-10 ℃/min, and the temperature is kept for 30-40 min; heating from 465-470 ℃ to 980-990 ℃ at a heating rate of 6-10 ℃/min, and preserving heat for 10-50 min; heating from 980-990 ℃ to 1240-1260 ℃ at a heating rate of 3-5 ℃/min, and preserving the heat for 100-120 min. Most preferably, the method comprises heating from room temperature to 465 ℃ at a heating rate of 10 ℃/min, and keeping the temperature for 30 min; raising the temperature from 465 ℃ to 980 ℃ at the heating rate of 10 ℃/min, and preserving the temperature for 10-40 min; heating from 980 ℃ to 1240 ℃ at the heating rate of 3 ℃/min, and preserving the heat for 120 min.
In the present invention, the function of controlling the vacuum brazing within the above-described procedure is to ensure that the joint is welded through.
In the present invention, the vacuum brazing is preferably performed in a vacuum heat treatment furnace.
After the vacuum brazing is completed, the invention also preferably comprises cooling, and the cooling mode is preferably furnace cooling.
To obtain post-weld Ni3After Al-based single crystal alloy, the invention uses the welded Ni3Heat treating Al-base monocrystal alloy to obtain Ni3A weldment of Al-based single crystal alloy.
In the invention, the temperature of the heat treatment is 1050-1100 ℃, preferably 1060-1080 ℃; the time is preferably 8-12 h, and more preferably 10 h.
In the present invention, the heat treatment is preferably performed in a tube furnace.
After the heat treatment is completed, the present invention also preferably includes cooling; the cooling is preferably air cooling.
The following examples are provided to illustrate the present invention3The post-welding treatment method of the Al-based single crystal alloy will be described in detail, but it should not be construed that the scope of the present invention is limited thereto.
Example 1
Cutting the thermally treated IC21 single crystal rod into alloy blocks, grinding the section, and ultrasonically cleaning with acetone for 15 min. Then, the two alloy blocks are fixed by a butt joint tool, the gap is controlled to be 50 mu m, a platinum sheet is adopted for spot welding, and then brazing filler metal (B:1 wt%, Si:3 wt%, Ti:7 wt%, Al:3 wt%, Co:9 wt%, W:4 wt%, Cr:11 wt%, and Ni: the balance) is coated and welded around the joint to obtain the pretreated IC21 alloy;
placing the pretreated IC21 in a vacuum heat treatment furnace, and vacuumizing to less than or equal to 7 x 10-3After Pa, heating from room temperature to 465 ℃ at the heating rate of 10 ℃/min, and keeping the temperature for 30 min; heating from 465 ℃ to 980 ℃ at the heating rate of 10 ℃/min, and preserving heat for 10 min; heating up from 980 ℃ to 1240 ℃ at the heating rate of 3 ℃/min, preserving heat for 120min, and then cooling along with the furnace to obtain the post-welded Ni3An Al-based single crystal alloy;
subjecting the post-weld Ni3Placing the Al-based single crystal alloy in a tube furnace, carrying out heat treatment at 1050 ℃ for 10h, and air cooling to obtain Ni3A weldment of an Al-based single crystal alloy (wherein the temperature control process of the brazing process and the post-weld heat treatment is shown in fig. 1);
dissecting the Ni3Welding joints of welding pieces of the Al-based single crystal alloy, observing joint structures through a metallographic microscope, and testing the tensile strength according to GB/T228.2-2015 standard;
the Ni3As shown in FIG. 2, the metallographic structure of the weld joint of the Al-based single crystal alloy weld material was as shown in FIG. 2, and it can be seen from FIG. 2 that Ni was contained in the weld material3The isothermal solidification region of the welding joint of the Al-based single crystal alloy welding part is wider, which reaches 68 percent of the welding line, the matrix structure is uniform, and the boride phase is dispersed;
the Ni3The tensile strength of a welded part of the Al-based single crystal alloy is 649MPa at 980 ℃, and the Ni is welded without heat treatment3The tensile strength of the Al-based single crystal alloy at 980 ℃ was 513MPa, from which it can be seen that the Ni3The tensile strength of the welding part of the Al-based single crystal alloy is higher than that of the non-heat-treated post-welding Ni3Tensile strength of the Al-based single crystal alloy.
Example 2
Cutting the thermally treated IC21 single crystal rod into alloy blocks, grinding the section, and ultrasonically cleaning with acetone for 15 min. Then, the two alloy blocks are fixed by a butt joint tool, the gap is controlled to be 50 mu m, a platinum sheet is adopted for spot welding, and then brazing filler metal (B:1 wt%, Si:3 wt%, Ti:7 wt%, Al:3 wt%, Co:9 wt%, W:4 wt%, Cr:11 wt%, and Ni: the balance) is coated and welded around the joint to obtain the pretreated IC21 alloy;
placing the pretreated IC21 in a vacuum heat treatment furnace, and vacuumizing to less than or equal to 7 x 10-3After Pa, heating from room temperature to 465 ℃ at the heating rate of 10 ℃/min, and keeping the temperature for 30 min; heating from 465 ℃ to 980 ℃ at the heating rate of 10 ℃/min, and preserving heat for 10 min; heating up from 980 ℃ to 1240 ℃ at the heating rate of 3 ℃/min, preserving heat for 120min, and then cooling along with the furnace to obtain the post-welded Ni3An Al-based single crystal alloy;
subjecting the post-weld Ni3Placing the Al-based single crystal alloy in a tube furnace, carrying out heat treatment at 1100 ℃ for 10h, and air cooling to obtain Ni3A weldment of an Al-based single crystal alloy (wherein the temperature control process of the brazing process and the post-weld heat treatment is shown in fig. 1);
the Ni3As shown in FIG. 3, the metallographic structure of the weld joint of the Al-based single crystal alloy weld material was as shown in FIG. 3, and it can be seen from FIG. 3 that Ni was contained in the weld material3The isothermal solidification region of a welding joint of the Al-based single crystal alloy welding part is wider, which reaches 60 percent of a welding seam, the matrix structure is uniform, and boride phases are dispersed;
the Ni3The tensile strength of a welded part of the Al-based single crystal alloy at 980 ℃ is 667MPa, and the Ni is welded without heat treatment3The tensile strength of the Al-based single crystal alloy at 980 ℃ was 495MPa, from which it can be seen that the Ni3The tensile strength of the welding part of the Al-based single crystal alloy is higher than that of the non-heat-treated post-welding Ni3Tensile strength of the Al-based single crystal alloy.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
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