NiCoCrHfB (Fe, Ti, Zr, Nb) brazing filler metal and application thereof

Abstract

The invention provides a NiCoCrHfB (Fe, Ti, Zr and Nb) brazing filler metal and application of the NiCoCrHfB (Fe, Ti, Zr and Nb) brazing filler metal. The brazing filler metal comprises the following components in percentage by mass: 12.0-24.0% of Co; 2.0 to 8.0% of Cr; 16.0 to 32.0 percent of Hf (hydrogen fluoride); 0 to 4.0% of Fe; 0 to 4.5% of Ti; 0 to 4.0% of Zr; 0 to 5.0 percent of Nb; 1.0 to 3.0 percent of B; and the balance Ni. Through research, when the brazing filler metal is applied to brazing of a TiAl-based alloy and other non-TiAl-based alloys, an obtained brazed joint has high high-temperature strength, for example, a TiAl / GH3536 brazed joint obtained under the condition of (1140-1180) DEG C / (10-30) min has the high-temperature shear strength of 355-422 MPa and the high-temperature shear strength of 308-348 MPa at the temperature of 750 DEG C and the high-temperature shear strength of 308-348 MPa at the temperature of 850 DEG C.

Description

TECHNICAL FIELD

[0001] The application belongs to the technical field of aviation brazing, and particularly relates to a NiCoCrHfB(Fe, Ti, Zr, Nb) filler metal and application thereof, in particular to a NiCoCrHfB(Fe, Ti, Zr, Nb) filler metal for connecting a TiAl-based alloy and a GH3536 high-temperature alloy and application thereof. BACKGROUND

[0002] Compared with traditional nickel-based high-temperature alloys, TiAl-based alloys not only have the advantage of low density (3.7-3.9 g·cm -3 ), but also have a comparable elastic modulus, a higher creep limit and good high-temperature oxidation resistance, and can withstand a working temperature of 750-850 DEG C for a long time. Therefore, the use of TiAl-based alloys to partially replace nickel-based high-temperature alloys can achieve structural weight reduction and improve flight efficiency, which is conducive to achieving the goal of energy saving and emission reduction, and has a good engineering application prospect in the aviation field.

[0003] In addition to the connection requirements of TiAl-based alloys, the application of TiAl-based alloys also needs to further solve the heterogeneous connection requirements of TiAl and nickel-based high-temperature alloys. However, due to the differences in chemical composition and physical properties between TiAl-based alloys and nickel-based high-temperature alloys, the metallurgical compatibility of different alloy elements in the joint is poor, and the thickness of the brittle reaction layer at the connection interface is difficult to effectively control, which increases the residual stress in the joint, thereby seriously affecting the joint strength.

[0004] At present, brazing is considered to be a method suitable for the heterogeneous connection of TiAl-based alloys and nickel-based high-temperature alloys. Compared with other welding or connection methods, brazing technology has significant comprehensive advantages in controlling the generation of brittle phases at the heterogeneous interface, relieving the internal stress of the joint and improving the structural adaptability. However, the room temperature / high-temperature strength of the joint obtained by using existing noble metal-based, Ti-based, Zr-based, Ni-based and Fe-based filler metals cannot meet the high-temperature use requirements of 750-850 DEG C. SUMMARY

[0005] Therefore, the purpose of the present application is to provide a NiCoCrHfB(Fe, Ti, Zr, Nb) filler metal and application thereof, in particular to provide a NiCoCrHfB(Fe, Ti, Zr, Nb) filler metal for connecting a TiAl-based alloy and a GH3536 high-temperature alloy and application thereof. The filler metal can effectively solve the problems of excessively high brazing temperature of the brazing filler metal and insufficient room temperature / high-temperature (750-850 DEG C) strength of the brazed joint in the prior art.

[0006] To achieve this purpose, the present application adopts the following technical solutions:

[0007] In a first aspect, the present application provides a NiCoCrHfB(Fe, Ti, Zr, Nb) filler metal, comprising the following components in mass percentage:

[0008] Co 12.0-24.0%; Cr 2.0-8.0%; Hf 16.0-32.0%; Fe 0-4.0%; Ti 0-4.5%; Zr 0-4.0%; Nb 0-5.0%; B 1.0-3.0%; balance Ni.

[0009] Preferably, comprising Co 14.0-24.0%; Cr 2.0-6.0%; Hf 19.0-29.0%; Fe 0-4.0%; Ti 0-4.5%; Zr 0-4.0%; Nb 0-5.0%; B 1.0-3.0%; balance Ni in mass percentage.

[0010] Preferably, the NiCoCrHfB(Fe, Ti, Zr, Nb) filler metal comprises the following components in mass percentage:

[0011] Co 24.0%, Cr 2.0%, Hf 16.0%, B 1.0%, Nb 5.0%, Ti 4.5%, Zr 4.0%, Fe 0%, Ni 43.5%;

[0012] or Co 23.0%, Cr 3.0%, Hf 17.0%, B 1.4%, Nb 4.5%, Ti 4.5%, Zr 4.0%, Fe 0%, Ni 42.6%;

[0013] or Co 22.0%, Cr 2.0%, Hf 18.0%, B 1.7%, Nb 4.0%, Ti 4.0%, Zr 4.0%, Fe 0%, Ni 44.3%;

[0014] or Co 20.0%, Cr 3.0%, Hf 20.0%, B 2.0%, Nb 3.5%, Ti 3.5%, Zr 3.5%, Fe 0%, Ni 44.50%;

[0015] or Co 19.0%, Cr 4.0%, Hf 22.0%, B 2.3%, Nb 3.0%, Ti 3.0%, Zr 3.0%, Fe 0%, Ni 43.70%;

[0016] or Co 17.0%, Cr 5.0%, Hf 24.0%, B 2.6%, Nb 2.5%, Ti 2.5%, Zr 2.5%, Fe 0%, Ni 43.90%;

[0017] or Co 15.0%, Cr 6.0%, Hf 26.0%, B 3.0%, Nb 2.0%, Ti 2.0%, Zr 2.0%, Fe 0%, Ni 44.00%;

[0018] or Co 13.0%, Cr 8.0%, Hf 28.0%, B 1.4%, Nb 1.5%, Ti 1.5%, Zr 1.5%, Fe 0%, Ni 45.10%;

[0019] or Co 14.0%, Cr 7.0%, Hf 30.0%, B 1.7%, Nb 1.0%, Ti 1.0%, Zr 1.0%, Fe 0%, Ni 44.30%;

[0020] or Co 12.0%, Cr 7.0%, Hf 32.0%, B 2.0%, Nb 0.5%, Ti 0.5%, Zr 0.5%, Fe 0%, Ni 45.50%;

[0021] or Co 22.0%, Cr 2.0%, Hf 19.0%, B 1.0%, Nb 5.0%, Ti 4.5%, Zr 0%, Fe 0%, Ni 46.50%;

[0022] or Co 20.0%, Cr 3.0%, Hf 23.0%, B 1.7%, Nb 3.0%, Ti 3%, Zr 0%, Fe 0%, Ni 46.30%;

[0023] or Co 18.0%, Cr 4.0%, Hf 25.0%, B 2.0%, Nb 2.0%, Ti 2%, Zr 0%, Fe 0%, Ni 47.00%;

[0024] or Co 16.0%, Cr 5.0%, Hf 27.0%, B 2.6%, Nb 1.0%, Ti 1%, Zr 0%, Fe 0%, Ni 47.40%;

[0025] or Co 12.0%, Cr 6.0%, Hf 31.0%, B 3.0%, Nb 0.50%, Ti 0.50%, Zr 0%, Fe 0%, Ni 47.00%;

[0026] or Co 24.0%, Cr 2.0%, Hf 29.0%, B 1.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 44.00%;

[0027] or Co 21.0%, Cr 4.0%, Hf 25.6%, B 1.7%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 47.70%;

[0028] or Co 20.0%, Cr 5.0%, Hf 23.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 50.00%;

[0029] or Co 16.0%, Cr 6.0%, Hf 21.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 54.40%;

[0030] or Co 12.0%, Cr 8.0%, Hf 16.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 61.00%;

[0031] or Co 24.0%, Cr 2.0%, Hf 16.0%, B 1.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0.5%, Ni 56.50%;

[0032] or Co 23.0%, Cr 3.0%, Hf 17.0%, B 1.4%, Nb 0%, Ti 0%, Zr 0%, Fe 1.0%, Ni 54.60%;

[0033] or Co 22.0%, Cr 2.0%, Hf 18.0%, B 1.7%, Nb 0%, Ti 0%, Zr 0%, Fe 1.5%, Ni 54.80%;

[0034] or Co 20.0%, Cr 3.0%, Hf 20.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 2.0%, Ni 53.00%;

[0035] or Co 19.0%, Cr 4.0%, Hf 22.0%, B 2.3%, Nb 0%, Ti 0%, Zr 0%, Fe 2.3%, Ni 50.40%;

[0036] or Co 17.0%, Cr 5.0%, Hf 24.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 2.5%, Ni 48.90%;

[0037] Or Co 15.0%, Cr 6.0%, Hf 26.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 2.8%, Ni 47.20%;

[0038] Or Co 13.0%, Cr 8.0%, Hf 28.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 3.0%, Ni 46.00%;

[0039] Or Co 14.0%, Cr 7.0%, Hf 30.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 3.5%, Ni 42.90%;

[0040] Or Co 12.0%, Cr 7.0%, Hf 32.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 4.0%, Ni 42.00%.

[0041] Preferably, the brazing filler metal is used in one or more of the following forms: block, granular, sheet, powder, amorphous foil strip, or powder sintered body.

[0042] Secondly, the present invention provides an application of the above-mentioned NiCoCrHfB(Fe,Ti,Zr,Nb) solder in the heterojunction of TiAl-based alloys and non-TiAl-based alloys;

[0043] The non-TiAl based alloys include, but are not limited to, any one or more of nickel-based superalloys, iron-nickel-based alloys, or cobalt-based superalloys.

[0044] Preferably, the nickel-based superalloy includes, but is not limited to, any one or more of GH3536 superalloy, GH3230 superalloy, GH4169 superalloy, or K24 superalloy.

[0045] Preferably, the cobalt-based superalloy includes, but is not limited to, GH5188.

[0046] Thirdly, the present invention provides a brazing method for TiAl-based alloys and non-TiAl-based alloys, comprising the following steps:

[0047] S1. Assembly: Add solder to the soldering positions between TiAl-based alloy base material and non-TiAl-based alloy base material to obtain an assembly component; the solder is the NiCoCrHfB(Fe,Ti,Zr,Nb) solder involved in the above technical solution; the non-TiAl-based alloy includes, but is not limited to, any one or more of nickel-based superalloys, iron-nickel-based alloys, or cobalt-based superalloys.

[0048] S2, Brazing: Brazing the assembly components.

[0049] Preferably, the brazing is performed using vacuum brazing.

[0050] Preferably, the vacuum degree of the vacuum brazing is better than 7×10⁻⁶. -3 Pa.

[0051] Preferably, the vacuum brazing temperature is 1140–1180°C and the time is 10–30 min.

[0052] More preferably, the vacuum brazing process involves heating at a rate of 10–20 °C / min to 600 °C; then heating at a rate of 10–30 °C / min to 900 °C; then heating at a rate of 10–25 °C / min to 1140–1180 °C and holding at that temperature for 10–30 min; after holding at that temperature, the temperature is slowly reduced to 600 °C at a rate of 5–10 °C / min, and then further reduced at a rate of 10–20 °C / min and cooled in the furnace.

[0053] Preferably, the brazing gap at the position to be welded is 0.04 to 0.08 mm.

[0054] Preferably, when the non-TiAl-based alloy is GH3536 high-temperature alloy, the brazed joint obtained after brazing in step S2 has a shear strength of 376-445 MPa at room temperature; a shear strength of 355-422 MPa at 750°C; and a shear strength of 308-348 MPa at 850°C.

[0055] Compared with the prior art, the beneficial effects of the present invention are as follows:

[0056] This invention provides a NiCoCrHfB(Fe,Ti,Zr,Nb) solder, comprising the following components by mass percentage: Co 12.0–24.0%; Cr 2.0–8.0%; Hf 16.0–32.0%; Fe 0–4.0%; Ti 0–4.5%; Zr 0–4.0%; Nb 0–5.0%; B 1.0–3.0%; balance Ni.

[0057] Studies have shown that the NiCoCrHfB(Fe,Ti,Zr,Nb) brazing filler metal exhibits certain solid solution strengthening and grain refinement effects when applied to brazing TiAl-based alloys with other non-TiAl-based alloys, resulting in brazed joints with high room temperature / high temperature strength. Tests revealed that the room temperature shear strength of brazed joints obtained from TiAl-based alloys / GH3536 high-temperature alloys at (1140–1180)℃ / (10–30)min reached 376–445 MPa, while the high-temperature shear strengths at 750℃ and 850℃ were 355–422 MPa and 308–348 MPa, respectively. Attached Figure Description

[0058] Figure 1 The microstructure of the as-cast alloy of the brazing filler prepared in Example 3;

[0059] Figure 2 The microstructure of the as-cast alloy of the brazing filler prepared in Example 14;

[0060] Figure 3 The microstructure of the as-cast alloy of the brazing filler prepared in Example 23;

[0061] Figure 4 The cross-sectional microstructure of the brazed joint prepared in Example 3;

[0062] Figure 5 Microstructure of the cross-section of the brazed joint prepared in Example 14;

[0063] Figure 6 Microstructure of the cross-section of the brazed joint prepared in Example 23;

[0064] Figure 7 The X-ray diffraction (XRD) pattern of the amorphous foil ribbon prepared in Example 3;

[0065] Figure 8 The Ni-Hf binary phase diagram;

[0066] Figure 9 The Ni-Ti binary phase diagram;

[0067] Figure 10 The Ni-Nb binary phase diagram;

[0068] Figure 11 This is a Ni-Zr binary phase diagram. Detailed Implementation

[0069] The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those of ordinary skill in the art without creative effort are within the scope of protection of the present invention.

[0070] To address the problem of insufficient joint strength after brazing in existing brazing filler metals, this invention considers the metallurgical effects of various elements during the experimental process and proposes a NiCoCrHfB(Fe,Ti,Zr,Nb) brazing filler metal, which comprises the following components by mass percentage:

[0071] Co 12.0–24.0%; Cr 2.0–8.0%; Hf 16.0–32.0%; Fe 0–4.0%; Ti 0–4.5%; Zr 0–4.0%; Nb 0–5.0%; B 1.0–3.0%; balance Ni.

[0072] The aforementioned Co content of 12.0% to 24.0% can be 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19%, 20%, 21%, 22%, 23%, or 24%.

[0073] Cr 2.0%–8.0%, which can be 2%, 3%, 4%, 5%, 6%, 7% or 8%.

[0074] Hf 16.0%–32.0%, which can be 16%, 17%, 18%, 19%, 20%, 21%, 22%, 23%, 24%, 25%, 26%, 27%, 28%, 29%, 30%, 31%, or 32%.

[0075] Fe 0–4.0%, which can be 0%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, or 4%, etc., preferably 0–3.5%.

[0076] Ti 0 to 4.5%, which can be 0%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, or 4.5%, etc.

[0077] Zr content is 0–4.0%, and can be 0%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, or 4%, etc., preferably 0–3.5%.

[0078] Nb 0–5.0%, which can be 0%, 0.5%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, or 5%, etc.

[0079] B 1.0%~3.0%, which can be 1%, 1.4%, 1.7%, 2%, 2.3%, 2.6% or 3%, etc.

[0080] Preferably, the NiCoCrHfB(Fe,Ti,Zr,Nb) solder comprises, by mass percentage: Co 14.0–24.0%; Cr 2.0–7.0%; Hf 19.0–29.0%; Fe 0–4.0%; Ti 0–4.5%; Zr 0–4.0%; Nb 0–5.0%; B 1.0–3.0%; balance Ni.

[0081] In some embodiments of the present invention, the NiCoCrHfB(Fe,Ti,Zr,Nb) solder comprises, by mass fraction:

[0082] Co 24.0%, Cr 2.0%, Hf 16.0%, B 1.0%, Nb 5.0%, Ti 4.5%, Zr 4.0%, Fe0%, Ni 43.5%;

[0083] Or Co 23.0%, Cr 3.0%, Hf 17.0%, B 1.4%, Nb 4.5%, Ti 4.5%, Zr 4.0%, Fe 0%, Ni 42.6%;

[0084] Or Co 22.0%, Cr 2.0%, Hf 18.0%, B 1.7%, Nb 4.0%, Ti 4.0%, Zr 4.0%, Fe 0%, Ni 44.3%;

[0085] Or Co 20.0%, Cr 3.0%, Hf 20.0%, B 2.0%, Nb 3.5%, Ti 3.5%, Zr 3.5%, Fe 0%, Ni 44.50%;

[0086] Or Co 19.0%, Cr 4.0%, Hf 22.0%, B 2.3%, Nb 3.0%, Ti 3.0%, Zr 3.0%, Fe 0%, Ni 43.70%;

[0087] Or Co 17.0%, Cr 5.0%, Hf 24.0%, B 2.6%, Nb 2.5%, Ti 2.5%, Zr 2.5%, Fe 0%, Ni 43.90%;

[0088] Or Co 15.0%, Cr 6.0%, Hf 26.0%, B 3.0%, Nb 2.0%, Ti 2.0%, Zr 2.0%, Fe 0%, Ni 44.00%;

[0089] Or Co 13.0%, Cr 8.0%, Hf 28.0%, B 1.4%, Nb 1.5%, Ti 1.5%, Zr 1.5%, Fe 0%, Ni 45.10%;

[0090] Or Co 14.0%, Cr 7.0%, Hf 30.0%, B 1.7%, Nb 1.0%, Ti 1.0%, Zr 1.0%, Fe 0%, Ni 44.30%;

[0091] Or Co 12.0%, Cr 7.0%, Hf 32.0%, B 2.0%, Nb 0.5%, Ti 0.5%, Zr 0.5%, Fe 0%, Ni 45.50%;

[0092] Or Co 22.0%, Cr 2.0%, Hf 19.0%, B 1.0%, Nb 5.0%, Ti 4.5%, Zr 0%, Fe 0%, Ni 46.50%;

[0093] Or Co 20.0%, Cr 3.0%, Hf 23.0%, B 1.7%, Nb 3.0%, Ti 3%, Zr 0%, Fe 0%, Ni 46.30%;

[0094] Or Co 18.0%, Cr 4.0%, Hf 25.0%, B 2.0%, Nb 2.0%, Ti 2%, Zr 0%, Fe 0%, Ni 47.00%;

[0095] Or Co 16.0%, Cr 5.0%, Hf 27.0%, B 2.6%, Nb 1.0%, Ti 1%, Zr 0%, Fe 0%, Ni 47.40%;

[0096] Or Co 12.0%, Cr 6.0%, Hf 31.0%, B 3.0%, Nb 0.50%, Ti 0.50%, Zr 0%, Fe 0%, Ni 47.00%;

[0097] Or Co 24.0%, Cr 2.0%, Hf 29.0%, B 1.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 44.00%;

[0098] Or Co 21.0%, Cr 4.0%, Hf 25.6%, B 1.7%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 47.70%;

[0099] Or Co 20.0%, Cr 5.0%, Hf 23.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 50.00%;

[0100] Or Co 16.0%, Cr 6.0%, Hf 21.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 54.40%;

[0101] Or Co 12.0%, Cr 8.0%, Hf 16.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 61.00%;

[0102] Or Co 24.0%, Cr 2.0%, Hf 16.0%, B 1.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0.5%, Ni 56.50%;

[0103] Or Co 23.0%, Cr 3.0%, Hf 17.0%, B 1.4%, Nb 0%, Ti 0%, Zr 0%, Fe 1.0%, Ni 54.60%;

[0104] Or Co 22.0%, Cr 2.0%, Hf 18.0%, B 1.7%, Nb 0%, Ti 0%, Zr 0%, Fe 1.5%, Ni 54.80%;

[0105] Or Co 20.0%, Cr 3.0%, Hf 20.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 2.0%, Ni 53.00%;

[0106] Or Co 19.0%, Cr 4.0%, Hf 22.0%, B 2.3%, Nb 0%, Ti 0%, Zr 0%, Fe 2.3%, Ni 50.40%;

[0107] Or Co 17.0%, Cr 5.0%, Hf 24.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 2.5%, Ni 48.90%;

[0108] Or Co 15.0%, Cr 6.0%, Hf 26.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 2.8%, Ni 47.20%;

[0109] Or Co 13.0%, Cr 8.0%, Hf 28.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 3.0%, Ni 46.00%;

[0110] Or Co 14.0%, Cr 7.0%, Hf 30.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 3.5%, Ni 42.90%;

[0111] Or Co 12.0%, Cr 7.0%, Hf 32.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 4.0%, Ni 42.00%.

[0112] In this invention, the composition design concept of the above-mentioned NiCoCrHfB(Fe,Ti,Zr,Nb) solder is as follows:

[0113] On the one hand, using Ni-Hf, Ni-B, and Co-B eutectic compositions can lower the melting point of the solder. For example, the eutectic temperature of the Ni-30.3Hf (wt%) alloy is 1190℃ (refer to...). Figure 8 The eutectic temperature of Ni-13.2B (wt%) alloy is 1018℃, and that of Co-4.0B (wt%) alloy is 1110℃. The Hf content ranges from 16.0% to 32.0% wt%, allowing the formation of Ni-Hf compounds. Since Ni-Hf compounds have lower hardness and better toughness compared to intermetallic compounds such as Ni-Al and Ni-Ti, the Ni-Hf compounds formed in the brazing seam are beneficial to the strength of the brazed joint. Furthermore, Hf is infinitely miscible with Ti and has some compatibility with Ni and Co; therefore, Hf has good compatibility with TiAl and nickel-based superalloys.

[0114] On the other hand, Ni also exhibits binary eutectic properties with alloying elements Ti, Zr, and Nb. For example, the eutectic temperature of Ni-20.8Ti (wt%) alloy is 943℃, that of Ni-46.7Zr (wt%) alloy is 1070℃, and that of Ni-51.9Nb (wt%) alloy is 1180℃, further reducing the melting point of the solder in this system (see reference). Figures 9-11 ).

[0115] Tests have shown that the liquidus temperature T of the solder described above in this invention is... L With a temperature range of 1113.80–1140.60℃, it can achieve low-temperature brazing (T b =1140~1180℃). Conversely, if the liquidus temperature T of the solder is... L Too high, natural brazing temperature T bThis will also be higher, resulting in not only excessive energy consumption during brazing production, but also excessively high T. b The microstructure of the brazing weld zone and the degree of interfacial reaction can be affected, which can also significantly impair the properties of the base material. Furthermore, the degree of interfacial reaction can be further reduced by adding a small amount of Fe (0–4.0 wt%) to the aforementioned brazing filler metal.

[0116] The mixing entropy (ΔS) of NiCoCrHfB(Fe,Ti,Zr,Nb) alloy solder was calculated using thermodynamics. mix The concentration ranges from 9.20 to 12.16 J·mol⁻¹ -1 ·K -1 Between these parameters, the key parameter ΔS of the multi-principal element alloy is satisfied. mix The requirement, namely the ΔS of medium-entropy alloys mix (1.0R~1.5R (R is the gas constant)), therefore, the alloy solder is determined to be a medium-entropy alloy. Due to the compositional characteristics of the multi-element medium-entropy alloy, the solder of the present invention will not undergo a violent interfacial reaction with the base material being soldered (TiAl-based alloys and non-TiAl-based alloys, such as GH3535 alloy), thus facilitating the obtaining of a good metallurgical bond.

[0117] In addition, Ni, Co, and Cr, as commonly used high-temperature alloying elements in high-temperature alloys, not only have good metallurgical compatibility with non-TiAl-based alloys, such as GH3535 alloy, but also can strengthen TiAl alloys to a certain extent within a certain content range. For example, Ni promotes dynamic recrystallization of TiAl alloys, Co can refine grains and improve the strength of TiAl alloys, while Cr can significantly improve the strength and toughness of TiAl alloy joints. Considering that the Cr content in TiAl-based alloys is generally 2.0–6.0 wt%, the recommended Cr content of the brazing filler metal in this invention is 2.0–6.0 wt%. Furthermore, the Co content in the brazing filler metal is intentionally designed to be 12.0–24.0 wt%. Fe improves the mechanical properties of TiAl joints through grain refinement and solid solution strengthening; the designed Fe content in the brazing filler metal of this invention is 0–4.0 wt%. Therefore, this invention utilizes the design concept of multi-element medium-entropy alloys, incorporating the above-mentioned alloying elements in the design of the brazing filler metal, and comprehensively utilizing the solid solution strengthening and grain refinement strengthening effects of different elements to improve the strength of the brazed joint.

[0118] Furthermore, the brazing filler metal of this invention does not contain Cu, an element with a low melting point, which is detrimental to the high-temperature performance of high-temperature alloys. Therefore, using the brazing filler metal of this invention, the retention rate of the room temperature strength of the obtained heterogeneous brazed joint at 750°C and 850°C can reach 90% and 80%, respectively. This brazed joint still has good heat resistance at the extreme service temperature (850°C) of the TiAl base material. The TiAl-based alloy / GH3536 high-temperature alloy brazed joint obtained by the brazing filler metal of this invention exhibits significantly better high-temperature strength in the temperature range of 750–850°C than the brazed joints corresponding to conventional Ti-based, Zr-based, Fe-based, and Ni-based brazing filler metal alloys.

[0119] Furthermore, this invention significantly enhances the amorphous forming capability of the solder foil by adding Hf element. The amorphous foil allows for precise control of the amount of solder added, thereby improving assembly accuracy. Therefore, this invention is also highly suitable for the precision assembly and connection of complex components.

[0120] This invention also provides an application of the above-mentioned brazing filler metal in the heterojunction of TiAl-based alloys and non-TiAl-based alloys. The non-TiAl-based alloys include, but are not limited to, any one or more of nickel-based superalloys, iron-nickel-based alloys, or cobalt-based superalloys.

[0121] In this invention, the nickel-based superalloys include, but are not limited to, any one or more of GH3536 superalloy, GH3230 superalloy, GH4169 superalloy or K24 superalloy; the cobalt-based superalloys include, but are not limited to, GH5188.

[0122] This invention also provides a brazing method for TiAl-based alloys and non-TiAl-based alloys, comprising the following steps:

[0123] S1. Assembly: Add solder to the welding positions between the TiAl-based alloy base material and the non-TiAl-based alloy base material to obtain the assembly assembly; the solder is the solder involved in the above technical solution; the non-TiAl-based alloy includes, but is not limited to, any one or more of nickel-based high-temperature alloys, iron-nickel-based alloys, or cobalt-based high-temperature alloys;

[0124] S2, Brazing: Brazing the assembly components.

[0125] According to the present invention, TiAl-based alloy base materials and non-TiAl-based alloy base materials are first provided.

[0126] In some embodiments of the present invention, it is preferable to pre-treat the TiAl-based alloy base material and the non-TiAl-based alloy base material and the welding positions therebetween.

[0127] The pretreatment refers to sanding the surface to be welded with sandpaper and then cleaning it with alcohol or acetone to remove oil stains.

[0128] In this invention, the brazing filler metal is first prepared by mixing each element according to the formula in mass percentage and melting it using an electric arc melting method to obtain an alloy ingot; then, the alloy ingot is prepared into brazing filler metals with different shapes using different manufacturing processes. The shape can be one or more of the following forms: block, granular (fragmented granules), flake (thin sheet), powder (alloy powder), amorphous foil strip, or powder sintered body.

[0129] Then, according to the present invention, brazing filler metal is added to the welding position between the TiAl-based alloy base material and the non-TiAl-based alloy base material to obtain an assembly. For example, for amorphous foil, brazing filler metal foil with a thickness of 0.04 to 0.08 mm can be cut into foil sheets of appropriate area, spot welded to one side of the base material to be welded using a spot welding machine, and then the base materials on both sides can be clamped with a tooling to control the brazing gap to 0.04 to 0.08 mm, thus forming an assembly. For bulk brazing filler metal, powder sintered brazing filler metal, and powder brazing filler metal, the brazing gap can be controlled to 0.04 to 0.08 mm, and then the base material to be welded can be clamped with a tooling, and the bulk brazing filler metal, powder sintered brazing filler metal, and powder brazing filler metal can be fixed at the welding position of the base material to form an assembly.

[0130] The aforementioned 0.04–0.08 mm can be 0.04 mm, 0.05 mm, 0.06 mm, 0.07 mm, or 0.08 mm, etc.

[0131] Then, according to the present invention, the assembly components are brazed.

[0132] In this invention, the brazing is preferably performed in a vacuum furnace, and the vacuum degree of the vacuum brazing is better than 7 × 10⁻⁶. -3 Pa; the vacuum brazing temperature is 1140~1180℃, and the time is 10~30min.

[0133] In some embodiments of the present invention, the brazing conditions are preferably (1140~1180)℃ / (10~30)min; specifically, they can be (1140~1150)℃ / (10~30)min, (1150~1160)℃ / (10~30)min or (1160~1180)℃ / (10~30)min.

[0134] Preferably, in some specific embodiments of the present invention, the vacuum brazing is performed by heating at a rate of 10-20°C / min to 600°C; then heating at a rate of 10-30°C / min to 900°C; then heating at a rate of 10-25°C / min to 1140-1180°C and holding at that temperature for 10-30 min; after holding at that temperature, the temperature is slowly reduced to 600°C at a rate of 5-10°C / min, and then cooled at a rate of 10-20°C / min along with the furnace.

[0135] The above-mentioned 10~20℃ / min can be 10℃ / min, 11℃ / min, 12℃ / min, 13℃ / min, 14℃ / min, 15℃ / min, 16℃ / min, 17℃ / min, 18℃ / min, 19℃ / min or 20℃ / min, etc.

[0136] The 10-30℃ / min can be 10℃ / min, 12℃ / min, 15℃ / min, 17℃ / min, 20℃ / min, 22℃ / min, 25℃ / min, 27℃ / min, or 30℃ / min, etc.

[0137] The 10-25℃ / min can be 10℃ / min, 12℃ / min, 15℃ / min, 20℃ / min, 22℃ / min, or 25℃ / min, etc.

[0138] The 5-10℃ / min can be 5℃ / min, 6℃ / min, 7℃ / min, 8℃ / min, 9℃ / min, or 10℃ / min, etc.

[0139] The 10-30 min can be 10 min, 12 min, 15 min, 17 min, 20 min, 22 min, 25 min, 27 min, or 30 min, etc.

[0140] Tests showed that when the non-TiAl based alloy was GH3536 high-temperature alloy, the brazed joint obtained after brazing had a shear strength of 376–445 MPa at room temperature, a shear strength of 355–422 MPa at 750°C, and a shear strength of 308–348 MPa at 850°C.

[0141] Figures 1-3 The images show the microstructure of the as-cast brazing alloys prepared in Examples 3 (Ni-Co-Cr-Hf-Ti-Nb-Zr-B), 14 (Ni-Co-Cr-Hf-Ti-Nb-B), and 23 (Ni-Co-Cr-Hf-Fe-B) of this invention.

[0142] In these embodiments of the present invention, the as-cast microstructure of the solder of the present invention is mainly composed of Ni3B, Ni5Hf and CoNi phases, and there is an obvious Ni3B and CoNi eutectic structure in the interdendritic region.

[0143] Figures 4-6 The cross-sectional microstructures of brazed joints prepared in Examples 3 (Ni-Co-Cr-Hf-Ti-Nb-Zr-B), 14 (Ni-Co-Cr-Hf-Ti-Nb-B), and 23 (Ni-Co-Cr-Hf-Fe-B) of the present invention are shown respectively.

[0144] In Embodiment 3 of the present invention, the brazing filler metal of the present invention was used for brazing at (1140~1150)℃ / 30min. The brazed joint exhibited a multi-layer structure, which could be divided into five regions from the TiAl side to the GH3536 side, namely regions A, B, C, D and E. Among them, region A is adjacent to the TiAl base material, with a thickness of 18 μm, and is composed of B2 and α2-Ti3Al; region B is 10 μm thick and is mainly Al3NiTi2; region C is the main brazing seam region, with a thickness of 28 μm, and is mainly composed of AlNi2Ti, (Ti,Al,Ni,Cr,Mo) multi-component complex phases, Cr-rich (Cr,Ni,Fe) solid solution, CrMo, and Ni-rich (Ni,Cr,Fe) solid solution; region D is adjacent to the GH3536 side, with a thickness of 27 μm, and is mainly composed of CrFe phase and Ni-rich (Ni,Cr,Fe) solid solution; region E is 10 μm thick and is mainly composed of borides and (Ti,Nb,Hf)-(Ni,Co) intermetallic compounds.

[0145] In embodiments 14 and 23 of this invention, brazing was performed using the brazing filler metal of this invention at (1150–1160) °C / 20 min and (1170–1180) °C / 10 min, respectively. The brazed joints can also be divided into five regions, and the phase composition of the brazed weld seam remains basically unchanged. The difference is that the width of the brazed weld seam and the width of region D are both reduced.

[0146] To further illustrate the present invention, the following embodiments provide a detailed description. The experimental materials used in the following embodiments of the present invention are all commercially available products.

[0147] The component formulations and liquidus temperatures of the various solders used in the following examples are shown in Table 1 below:

[0148] Table 1

[0149]

[0150]

[0151] Examples 1-10

[0152] S1: According to the formulas of serial numbers 1 to 10 in Table 1, each element is prepared according to the mass percentage and melted by electric arc melting to obtain 10 sets of gold ingots.

[0153] S2: The 10 gold ingot combinations are prepared into brazing filler metals of different shapes using different manufacturing processes. Each gold ingot combination includes powder and amorphous foil strips.

[0154] S3: TiAl-based alloy and GH3536 alloy materials are used as the base materials, with nominal compositions of Ti-46Al-(3~4)Nb-(2~3)(Cr,Ta,B)(at.%) and Ni-(20.5~23)Cr-(17~20)Fe-(8~10)Mo-(1~4)(Co,W,C,Ti,Al)(wt%), respectively. For amorphous foil strips, 0.04~0.08mm thick brazing foil strips are cut into foil sheets of appropriate area, spot-welded to one side of the base material to be welded using a spot welding machine, and then the base materials on both sides are clamped with tooling. The brazing gap can be controlled at 0.04~0.08mm to form an assembly component. For powdered brazing filler metal, the brazing gap is controlled at 0.04~0.08mm, the base material to be welded is clamped with tooling, and powdered brazing filler metal is placed at the welding point of the base material to form an assembly component.

[0155] S4: Place the assembled components in a vacuum furnace for brazing. Increase the temperature at a rate of 15℃ / min to 600℃, then at a rate of 20℃ / min to 900℃, and finally at a rate of 15℃ / min to 1140–1150℃, holding for 30 minutes. The vacuum level inside the furnace is 4.3 × 10⁻⁶. -3 Pa; After the heat preservation is completed, the temperature is slowly reduced to 600℃ at a rate of 10℃ / min, and then cooled with the furnace at a rate of 10℃ / min to finally obtain the brazed joint.

[0156] The brazed joints obtained in Examples 1 to 10 were subjected to performance tests according to GB / T288-2021. The room temperature shear strength of the joints reached 389-442 MPa, and the shear strength of the brazed joints at high temperatures of 750℃, 800℃ and 850℃ were 377-422 MPa, 340-397 MPa and 309-348 MPa, respectively.

[0157] Examples 11-20

[0158] S1: According to the formulas of serial numbers 11 to 20 in Table 1, each element is weighed according to the mass percentage and melted by electric arc melting to obtain 10 sets of gold ingots;

[0159] S2: The 10 gold ingot combinations are prepared into brazing filler metals with different shapes using different manufacturing processes. Each gold ingot combination includes a block and an amorphous foil strip.

[0160] S3: Uses TiAl-based alloy and GH3536 alloy materials, with nominal compositions of Ti-48Al-2Nb-2Cr (at.%) and Ni-(20.5~23)Cr-(17~20)Fe-(8~10)Mo-(1~4)(Co,W,C,Ti,Al)(wt%), respectively. For amorphous foil strips, 0.04~0.08mm thick brazing foil strips are cut into foil sheets of appropriate area, spot-welded to one side of the base material to be welded using a spot welding machine, and then the base materials on both sides are clamped with tooling. The brazing gap can be controlled at 0.04~0.08mm to form an assembly component. For bulk brazing filler metal, the brazing gap is controlled at 0.04~0.08mm, and then the base material to be welded is clamped with tooling, and the bulk brazing filler metal is fixed at the welding point of the base material to form an assembly component.

[0161] S4: Place the assembled components in a vacuum furnace for brazing. Increase the temperature at a rate of 10℃ / min to 600℃, then at a rate of 15℃ / min to 900℃, and finally at a rate of 10℃ / min to 1150–1160℃, holding for 20 minutes. The vacuum level inside the furnace is 4.9 × 10⁻⁶. -3 Pa; After the heat preservation is completed, the temperature is slowly reduced to 600℃ at a rate of 9℃ / min, and then reduced at a rate of 12℃ / min and cooled with the furnace to finally obtain the brazed joint.

[0162] The present invention conducts performance tests on the brazed joints obtained above. The room temperature shear strength of the joints reaches 376-445 MPa, and the shear strengths of the brazed joints at high temperatures of 750℃, 800℃ and 850℃ are 355-422 MPa, 321-389 MPa and 308-348 MPa, respectively.

[0163] Examples 21-30

[0164] S1: According to the formulas in Table 1, serial numbers 21 to 30, each element is weighed according to the mass percentage and melted using the electric arc melting method to obtain 10 sets of gold ingots.

[0165] S2: The 10 gold ingot combinations are prepared into brazing filler metals with different shapes using different manufacturing processes. Each gold ingot combination includes a powder sintered body and an amorphous foil strip.

[0166] S3: Uses TiAl-based alloys and GH3536 alloy materials, with nominal compositions of Ti-46Al-(3~4)Nb-(2~3)(Cr,Ta,B)(at.%) and Ni-(20.5~23)Cr-(17~20)Fe-(8~10)Mo-(1~4)(Co,W,C,Ti,Al)(wt%), respectively. For amorphous foil strips, 0.04~0.08mm thick brazing foil strips are cut into foil sheets of suitable area, spot-welded to one side of the base material to be welded using a spot welding machine, and then the base materials on both sides are clamped with tooling. The brazing gap can be controlled at 0.04~0.08mm to form an assembly component. For powder sintered brazing filler metal, the brazing gap is controlled at 0.04~0.08mm, and then the base material to be welded is clamped with tooling, and the powder sintered brazing filler metal is fixed at the welding point of the base material to form an assembly component.

[0167] S4: Place the assembled components in a vacuum furnace for brazing. Increase the temperature at a rate of 20°C / min to 600°C, then at a rate of 25°C / min to 900°C, and finally at a rate of 20°C / min to 1160–1180°C, holding for 10 minutes. The vacuum level inside the furnace is 4.7 × 10⁻⁶. -3 Pa; After the heat preservation is completed, the temperature is slowly reduced to 600℃ at a rate of 10℃ / min, and then reduced at a rate of 15℃ / min and cooled with the furnace to finally obtain the brazed joint.

[0168] In Examples 24, 27-28 and 30, the brazing temperature was 1160-1170℃, and in Examples 21-23, 25-26 and 29, the brazing temperature was 1170-1180℃.

[0169] The joints obtained under conditions of (1170–1180)℃ / 10min exhibited an average room temperature shear strength of 389–440 MPa, with average shear strengths of 364–416 MPa, 318–387 MPa, and 310–342 MPa at high temperatures of 750℃, 800℃, and 850℃, respectively. The joints obtained under conditions of (1160–1170)℃ / 10min exhibited a room temperature shear strength of 382–431 MPa, with brazed joints exhibiting shear strengths of 368–395 MPa, 337–369 MPa, and 309–339 MPa at high temperatures of 750℃, 800℃, and 850℃, respectively.

[0170] As can be seen from the above embodiments, the average room temperature shear strength of the joint obtained using the brazing filler metal of the present invention under brazing conditions of (1170-1180)℃ / 10min reaches 389-440 MPa, and the average shear strength at high temperatures of 750℃, 800℃, and 850℃ is 364-416 MPa, 318-387 MPa, and 310-342 MPa, respectively. The room temperature shear strength of the joint obtained under conditions of (1160-1170)℃ / 10min reaches 382-431 MPa, and the shear strength of the brazed joint at high temperatures of 750℃, 800℃, and 850℃ is 368-395 MPa, 337-369 MPa, and 309-339 MPa, respectively. The room temperature shear strength of the joint obtained under the condition of (1150~1160)℃ / 20min reached 376~445MPa, and the shear strength of the brazed joint at high temperatures of 750℃, 800℃ and 850℃ were 355~422MPa, 321~389MPa and 308~348MPa, respectively. The room temperature shear strength of the joint obtained under the condition of (1140~1150)℃ / 30min reached 389~442MPa, and the shear strength of the brazed joint at high temperatures of 750℃, 800℃ and 850℃ were 377~422MPa, 340~397MPa and 309~348MPa, respectively.

[0171] Figure 1 The microstructure of the as-cast alloy of the brazing filler prepared in Example 3; Figure 2 The microstructure of the as-cast alloy of the brazing filler prepared in Example 14; Figure 3 The microstructure of the as-cast alloy of the brazing filler prepared in Example 23; Figure 4 The cross-sectional microstructure of the brazed joint prepared in Example 3; Figure 5 Microstructure of the cross-section of the brazed joint prepared in Example 14; Figure 6 Microstructure of the cross-section of the brazed joint prepared in Example 23; Figure 7 The image shows the X-ray diffraction (XRD) pattern of the amorphous foil prepared in Example 3. It can be seen that the brazing filler metal of this invention contains a considerable amount of Ni5Hf phase and exhibits good amorphous foil forming ability. After the filler metal fully reacts with the base materials on both sides of TiAl and the nickel-based superalloy, a multi-layered gradient transition structure is formed in the brazing seam.

[0172] Figure 8 The Ni-Hf binary phase diagram; Figure 9 The Ni-Ti binary phase diagram; Figure 10 The Ni-Nb binary phase diagram; Figure 11 The diagram shows the Ni-Zr binary phase diagram. It can be seen that Ni, Hf, and alloying elements Ti, Nb, and Zr can all form a low-melting-point eutectic composition, thereby lowering the melting point of the solder and helping to reduce the brazing temperature.

[0173] In summary, this invention provides a NiCoCrHfB (Fe,Ti,Zr,Nb) medium-entropy alloy brazing filler metal for joining TiAl-based alloys / GH3536 high-temperature alloys. By mass percentage, it comprises the following components: Co 12.0–24.0%; Cr 2.0–8.0%; Hf 16.0–32.0%; Fe 0–4.0%; Ti 0–4.5%; Zr 0–4.0%; Nb 0–5.0%; B 1.0–3.0%; balance Ni. By introducing the melting point-reducing element B or alloying elements Fe, Ti, Nb, and Zr into the Ni-Co-Cr-Hf matrix alloy and controlling the content of each component, this brazing filler metal, when applied to brazing TiAl-based alloys / GH3536 high-temperature alloys, results in brazed joints with lower brazing temperatures and higher room temperature / high-temperature shear strength.

[0174] The brazing filler metal provided by this invention, namely the NiCoCrHfB(Fe,Ti,Zr,Nb) medium-entropy alloy brazing filler metal for connecting TiAl-based alloys / GH3536 high-temperature alloys, is also suitable for connecting dissimilar materials such as TiAl-based composite materials and nickel-based, iron-nickel-based, or cobalt-based high-temperature alloys.

[0175] The above description of the disclosed embodiments enables those skilled in the art to make or use the invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the invention. Therefore, the invention is not to be limited to the embodiments shown herein, but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.

Claims

1. A NiCoCrHfB(Fe,Ti,Zr,Nb) solder, characterized in that, It comprises the following components by weight percentage: Co 12.0–24.0%; Cr 2.0–8.0%; Hf 16.0–32.0%; Fe 0–4.0%; Ti 0–4.5%; Zr 0–4.0%; Nb 0–5.0%; B 1.0–3.0%; balance Ni.

2. The NiCoCrHfB(Fe,Ti,Zr,Nb) solder according to claim 1, characterized in that, The brazing filler metal comprises, by mass percentage: Co 14.0–24.0%; Cr 2.0–6.0%; Hf 19.0–29.0%; Fe 0–4.0%; Ti 0–4.5%; Zr 0–4.0%; Nb 0–5.0%; B 1.0–3.0%; balance Ni.

3. The NiCoCrHfB(Fe,Ti,Zr,Nb) solder according to claim 1, characterized in that, The brazing filler metal, by mass fraction, comprises: Co 24.0%, Cr 2.0%, Hf 16.0%, B 1.0%, Nb 5.0%, Ti 4.5%, Zr 4.0%, Fe 0%, Ni43.5%; Or Co 23.0%, Cr 3.0%, Hf 17.0%, B 1.4%, Nb 4.5%, Ti 4.5%, Zr 4.0%, Fe 0%, Ni 42.6%; Or Co 22.0%, Cr 2.0%, Hf 18.0%, B 1.7%, Nb 4.0%, Ti 4.0%, Zr 4.0%, Fe 0%, Ni 44.3%; Or Co 20.0%, Cr 3.0%, Hf 20.0%, B 2.0%, Nb 3.5%, Ti 3.5%, Zr 3.5%, Fe 0%, Ni 44.50%; Or Co 19.0%, Cr 4.0%, Hf 22.0%, B 2.3%, Nb 3.0%, Ti 3.0%, Zr 3.0%, Fe 0%, Ni 43.70%; Or Co 17.0%, Cr 5.0%, Hf 24.0%, B 2.6%, Nb 2.5%, Ti 2.5%, Zr 2.5%, Fe 0%, Ni 43.90%; Or Co 15.0%, Cr 6.0%, Hf 26.0%, B 3.0%, Nb 2.0%, Ti 2.0%, Zr 2.0%, Fe 0%, Ni 44.00%; Or Co 13.0%, Cr 8.0%, Hf 28.0%, B 1.4%, Nb 1.5%, Ti 1.5%, Zr 1.5%, Fe 0%, Ni 45.10%; Or Co 14.0%, Cr 7.0%, Hf 30.0%, B 1.7%, Nb 1.0%, Ti 1.0%, Zr 1.0%, Fe 0%, Ni 44.30%; Or Co 12.0%, Cr 7.0%, Hf 32.0%, B 2.0%, Nb 0.5%, Ti 0.5%, Zr 0.5%, Fe 0%, Ni 45.50%; Or Co 22.0%, Cr 2.0%, Hf 19.0%, B 1.0%, Nb 5.0%, Ti 4.5%, Zr 0%, Fe 0%, Ni 46.50%; Or Co 20.0%, Cr 3.0%, Hf 23.0%, B 1.7%, Nb 3.0%, Ti 3%, Zr 0%, Fe 0%, Ni 46.30%; Or Co 18.0%, Cr 4.0%, Hf 25.0%, B 2.0%, Nb 2.0%, Ti 2%, Zr 0%, Fe 0%, Ni 47.00%; Or Co 16.0%, Cr 5.0%, Hf 27.0%, B 2.6%, Nb 1.0%, Ti 1%, Zr 0%, Fe 0%, Ni 47.40%; Or Co 12.0%, Cr 6.0%, Hf 31.0%, B 3.0%, Nb 0.50%, Ti 0.50%, Zr 0%, Fe 0%, Ni 47.00%; Or Co 24.0%, Cr 2.0%, Hf 29.0%, B 1.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 44.00%; Or Co 21.0%, Cr 4.0%, Hf 25.6%, B 1.7%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 47.70%; Or Co 20.0%, Cr 5.0%, Hf 23.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 50.00%; Or Co 16.0%, Cr 6.0%, Hf 21.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 54.40%; Or Co 12.0%, Cr 8.0%, Hf 16.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0%, Ni 61.00%; Or Co 24.0%, Cr 2.0%, Hf 16.0%, B 1.0%, Nb 0%, Ti 0%, Zr 0%, Fe 0.5%, Ni 56.50%; Or Co 23.0%, Cr 3.0%, Hf 17.0%, B 1.4%, Nb 0%, Ti 0%, Zr 0%, Fe 1.0%, Ni 54.60%; Or Co 22.0%, Cr 2.0%, Hf 18.0%, B 1.7%, Nb 0%, Ti 0%, Zr 0%, Fe 1.5%, Ni 54.80%; Or Co 20.0%, Cr 3.0%, Hf 20.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 2.0%, Ni 53.00%; Or Co 19.0%, Cr 4.0%, Hf 22.0%, B 2.3%, Nb 0%, Ti 0%, Zr 0%, Fe 2.3%, Ni 50.40%; Or Co 17.0%, Cr 5.0%, Hf 24.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 2.5%, Ni 48.90%; Or Co 15.0%, Cr 6.0%, Hf 26.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 2.8%, Ni 47.20%; Or Co 13.0%, Cr 8.0%, Hf 28.0%, B 2.0%, Nb 0%, Ti 0%, Zr 0%, Fe 3.0%, Ni 46.00%; Or Co 14.0%, Cr 7.0%, Hf 30.0%, B 2.6%, Nb 0%, Ti 0%, Zr 0%, Fe 3.5%, Ni 42.90%; Or Co 12.0%, Cr 7.0%, Hf 32.0%, B 3.0%, Nb 0%, Ti 0%, Zr 0%, Fe 4.0%, Ni 42.00%.

4. The NiCoCrHfB(Fe,Ti,Zr,Nb) solder according to any one of claims 1 to 3, characterized in that, The brazing filler metal is used in one or more of the following forms: block, granular, sheet, powder, amorphous foil strip, or powder sintered body.

5. The application of the NiCoCrHfB(Fe,Ti,Zr,Nb) solder according to any one of claims 1 to 4 in the heterojunction of TiAl-based alloys and non-TiAl-based alloys; The non-TiAl based alloys include, but are not limited to, any one or more of nickel-based superalloys, iron-nickel-based alloys, or cobalt-based superalloys.

6. The application according to claim 5, characterized in that, The nickel-based superalloys include, but are not limited to, any one or more of GH3536 superalloy, GH3230 superalloy, GH4169 superalloy, or K24 superalloy; The cobalt-based superalloys include, but are not limited to, GH5188.

7. A brazing method for TiAl-based alloys and non-TiAl-based alloys, characterized in that, Includes the following steps: S1. Assembly: Add solder to the soldering position between the TiAl-based alloy base material and the non-TiAl-based alloy base material to obtain the assembly assembly; the solder is NiCoCrHfB(Fe,Ti,Zr,Nb) solder as described in any one of claims 1 to 4; the non-TiAl-based alloy includes, but is not limited to, any one or more of nickel-based superalloys, iron-nickel-based alloys, or cobalt-based superalloys. S2, Brazing: Brazing the assembly components.

8. The brazing method according to claim 7, characterized in that, The brazing is performed using vacuum brazing. The vacuum degree of the vacuum brazing is better than 7×10. -3 Pa; The vacuum brazing temperature is 1140–1180℃, and the time is 10–30 min.

9. The brazing method according to claim 8, characterized in that, The vacuum brazing is performed according to the following procedure: Increase the temperature at a rate of 10–20℃ / min to 600℃; then increase the temperature at a rate of 10–30℃ / min to 900℃; then increase the temperature at a rate of 10–25℃ / min to 1140–1180℃ and hold for 10–30 min; after holding, slowly decrease the temperature at a rate of 5–10℃ / min to 600℃, then decrease the temperature at a rate of 10–20℃ / min and cool with the furnace. The brazing gap at the location to be welded is 0.04 to 0.08 mm.

10. The brazing method according to any one of claims 7 to 9, characterized in that, When the non-TiAl-based alloy is GH3536 high-temperature alloy, the brazed joint obtained after brazing in step S2 has a shear strength of 376-445 MPa at room temperature; a shear strength of 355-422 MPa at 750°C; and a shear strength of 308-348 MPa at 850°C.

Images