A high-carbide-content intermetallic compound alloy powder and its application

Abstract

This invention relates to a high-carbide-content intermetallic compound alloy powder and its applications, belonging to the field of laser processing materials technology. The high-carbide-content intermetallic compound alloy powder has the following chemical composition by mass percentage: Al 5.0%–5.8%, C 4.1%–4.6%, Cr 44.0%–46.0%, B 0.02%–0.04%, O ≤ 200 ppm, N ≤ 50 ppm, H ≤ 10 ppm, with the balance being Ni. The cladding layer prepared from the high-carbide-content intermetallic compound alloy powder of this invention is crack-free, has high hardness, and good wear resistance, meeting the surface performance requirements of key components in heavy-duty diesel engines.

Description

Technical Field

[0001] This invention relates to the field of laser processing materials technology, and in particular to an intermetallic compound alloy powder with high carbide content and its applications. Background Technology

[0002] Intermetallic compounds combine the thermal conductivity of metallic materials with the high hardness, high melting point, and excellent wear resistance of ceramic materials, making them a focus of attention. Among numerous intermetallic compounds, Ni3Al is widely used due to its excellent mechanical and high-temperature properties. Ni3Al intermetallic compounds are among the most promising high-temperature structural materials due to their low density, high melting point, high-temperature oxidation resistance, and good high-temperature wear resistance. However, with continuous industrial development, pure Ni3Al alloys can no longer meet the demands of modern industry as high-temperature wear-resistant materials. Research shows that adding ceramic reinforcing phases to Ni3Al can significantly improve the mechanical properties of Ni3Al-based cermets. A commonly used ceramic phase is chromium carbide particles, which have good wetting properties.

[0003] Existing patent literature discloses carbide-reinforced Ni3Al-based alloy powder and its laser cladding method. However, the average hardness of the cladding layer in existing solutions is only 550 HV to 610 HV, which is far from suitable for applications requiring high-load impact and high-temperature wear resistance (e.g., key components in mining machinery, metallurgy, and diesel engines). Therefore, improving the hardness and wear resistance of Ni3Al-based alloy cladding layers has become an urgent problem to be solved. Summary of the Invention

[0004] Based on the above analysis, the present invention aims to provide an intermetallic compound alloy powder with high carbide content and its application, in order to solve at least one of the following existing problems: (1) improving the hardness and wear resistance of the alloy powder and the cladding layer; (2) suppressing the formation of cladding defects during laser cladding.

[0005] The objective of this invention is mainly achieved through the following technical solutions:

[0006] This invention provides an intermetallic compound alloy powder with high carbide content. The chemical composition of the high-carbide-content intermetallic compound alloy powder, by mass percentage, is: Al

[0007] 5.0%–5.8%, C 4.1%–4.6%, Cr 44.0%–46.0%, B 0.02%–0.04%, O≤200ppm, N≤50ppm, H≤10ppm, balance Ni.

[0008] Furthermore, the microstructure of the intermetallic compound alloy powder with high carbide content includes Ni3Al phase, γ-Ni phase and carbides. The carbide structure mainly includes Cr7C3, and the mass content of carbides is 45% to 50%.

[0009] Furthermore, the ratio of nickel equivalent to aluminum equivalent in high carbide-content intermetallic compound alloy powders is 3.2 to 3.7.

[0010] Furthermore, the chemical composition of the high carbide content intermetallic compound alloy powder, by mass percentage, is: Al 5.3%–5.7%, C 4.2%–4.6%, Cr 44.5%–46.0%, B 0.02%–0.038%, O ≤190ppm, N ≤45ppm, H ≤7ppm, with the balance being Ni.

[0011] The present invention also provides a cladding layer with high carbide content, which is prepared using the above-mentioned intermetallic compound alloy powder with high carbide content.

[0012] The present invention also provides a method for preparing the above-mentioned high carbide content cladding layer, comprising the following steps:

[0013] Step 1: High-carbide-content intermetallic compound alloy powder is conveyed to the surface of the steel material using a coaxial powder feeding method;

[0014] Step 2: Use laser cladding to clad the surface of steel material with intermetallic compound alloy powder containing high carbide content, forming a cladding layer.

[0015] Furthermore, in step 1, the coaxial powder feeding rate is controlled to be 10g / min to 20g / min.

[0016] Furthermore, in step 2, the power of the laser cladding is controlled to be 1800W to 2600W, and the scanning speed is 0.13m / min to 0.30m / min.

[0017] Furthermore, the average hardness of the cladding layer is 800HV~1000HV, and the wear rate is...

[0018] ≤0.6×10 -5 mm 3 / (N·m).

[0019] The present invention also provides an application of intermetallic compound alloy powder with high carbide content, which is used for surface modification of steel or nickel-based alloy parts of heavy-duty diesel engines.

[0020] Compared with the prior art, the present invention can achieve at least one of the following beneficial effects:

[0021] 1) The high carbide content intermetallic compound alloy powder of the present invention has a high content of Cr7C3 reinforcing phase, and the cladding layer prepared by the alloy powder of the present invention has high hardness and good wear resistance.

[0022] 2) The high nickel-to-aluminum equivalent atomic ratio in the intermetallic compound alloy powder with high carbide content of the present invention reduces the cracking tendency of the cladding layer. The Ni3Al-based alloy cladding layer prepared on the surface of the parts has a dense structure, high bonding strength with the matrix, and good wear resistance, which can meet the surface performance requirements of key components in application environments such as high load impact and high temperature wear resistance.

[0023] 3) In the high carbide content intermetallic compound alloy powder of the present invention, the carbide Cr7C3 is fully melted and distributed in situ in a self-generated manner in the Ni3Al-based alloy powder, which can improve the uniformity of Cr7C3 distribution in the alloy powder; in the laser cladding method of the present invention, by precisely controlling the power and scanning speed of laser cladding, it is ensured that when the cladding layer is prepared by laser cladding technology, Cr7C3 melts and is formed again in situ, which can reduce the size of Cr7C3 and make Cr7C3 more uniformly distributed in the cladding layer.

[0024] Other features and advantages of the invention will be set forth in the description which follows, and will be apparent in part from the description, or may be learned by practicing the invention. The objects and other advantages of the invention may be realized and obtained by means of the structures particularly pointed out in the written description and the accompanying drawings. Attached Figure Description

[0025] The accompanying drawings are for illustrative purposes only and are not intended to limit the invention. Throughout the drawings, the same reference numerals denote the same parts.

[0026] Figure 1 This is a morphology diagram of the intermetallic compound alloy powder with high carbide content in Example 1 of the present invention;

[0027] Figure 2 This is a topographic image of the cladding layer in Embodiment 1 of the present invention;

[0028] Figure 3 This is a microstructure diagram of the cladding layer in Embodiment 1 of the present invention. Detailed Implementation

[0029] Preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, which form part of the present invention and, together with the embodiments of the present invention, serve to illustrate the principles of the present invention.

[0030] This invention provides an intermetallic compound alloy powder with high carbide content. The chemical composition of the high-carbide-content intermetallic compound alloy powder, by mass percentage, is: Al 5.0%–5.8%, C 4.1%–4.6%, Cr 44.0%–46.0%, B 0.02%–0.04%, O ≤ 200 ppm, N ≤ 50 ppm, H ≤ 10 ppm, with the balance being Ni. The microstructure of the above-mentioned high-carbide-content intermetallic compound alloy powder includes Ni3Al phase, γ-Ni phase, and carbides. The carbide structure mainly includes Cr7C3, with a carbide mass content of 45%–50%, and the γ-Ni phase mass content of 3.0%–9.0%. The carbides are diffusely distributed, and the length of the carbides is 9 μm–20 μm, for example, 9 μm–16 μm.

[0031] The high carbide content in the intermetallic compound alloy powder of the present invention can significantly improve the hardness of the powder, thereby increasing the hardness of the cladding layer prepared using the alloy powder, and providing a basis for the cladding layer to obtain good wear resistance.

[0032] Specifically, considering that the Cr7C3 carbide content in the high-carbide intermetallic compound alloy powder of the present invention is 45% to 50%, and that the Cr7C3 carbide content in the cladding layer is 40% to 50% when it is used to prepare the cladding layer, the high carbide ratio leads to a greater tendency for cladding defects such as cracks. Therefore, the atomic ratio of nickel equivalent to aluminum equivalent in the high-carbide intermetallic compound alloy powder of the present invention is controlled to be 3.2 to 3.7. By increasing the atomic ratio of nickel and aluminum equivalent, the formation of hardened NiAl phase can be suppressed, ensuring that the base phase of the cladding layer is Ni3Al phase and γ solid solution phase, thereby improving the plasticity of the base phase of the cladding layer and suppressing the formation of cladding defects.

[0033] Specifically, in this invention, the inventors, through in-depth research, proposed the following principle for calculating the number of nickel equivalent atoms:

[0034]

[0035] Where Ni represents the mass percentage of Ni element in intermetallic compound alloy powder with high carbide content, and Cr Ni3Al溶 It ranges from 3% to 7%.

[0036] The principle for calculating the equivalent atomic number of aluminum is as follows:

[0037]

[0038] Wherein, Al represents the mass percentage of Al element in the intermetallic compound alloy powder with high carbide content, and Cr... Ni3Al溶 It ranges from 3% to 7%.

[0039] Preferably, the ratio of nickel equivalent to aluminum equivalent in the high carbide content intermetallic compound alloy powder of the present invention is 3.2 to 3.5.

[0040] Specifically, as a preferred embodiment, the mass percentage of each component in the high carbide content intermetallic compound alloy powder of the present invention is as follows: Al 5.3%–5.7%, C 4.2%–4.6%, Cr 44.5%–46.0%, B 0.02%–0.038%, O ≤ 190 ppm, N ≤ 45 ppm, H ≤ 7 ppm, with the balance being Ni.

[0041] It should be noted that the high-carbide-content intermetallic alloy of the present invention contains a relatively large amount of Ni3Al, which exhibits room-temperature brittleness. A small amount of boron (B) can improve the room-temperature ductility of Ni3Al and inhibit crack formation. However, when B is excessive, it accumulates at the grain boundaries, promoting the formation of hot cracks. Within the chemical composition range of the high-carbide-content intermetallic alloy powder of the present invention, when the B content is below 0.02%, it cannot improve the plasticity of Ni3Al, while when the B content is above 0.04%, the cladding layer has a greater tendency to hot crack. Therefore, the B content of the present invention is determined to be 0.02% to 0.04%, which not only ensures the room-temperature ductility of the cladding layer but also inhibits the formation of hot cracks.

[0042] It should be noted that during the laser cladding process, impurity elements such as O, H, and N will participate in the metallurgical reaction of the high carbide content intermetallic compound alloy powder of the present invention. Excessive O content can easily lead to fatigue problems and increased wear; excessive N content can easily lead to AlN formation and increased cracking tendency; excessive H content increases the brittleness of the cladding layer. Therefore, the present invention controls O ≤ 200 ppm, N ≤ 50 ppm, and H ≤ 10 ppm.

[0043] Specifically, the high carbide content intermetallic compound alloy powder of the present invention is prepared by vacuum induction melting-inert gas atomization method.

[0044] Specifically, considering that if the particle size of the alloy powder is too large, unmelted powder will appear during laser cladding, while if the particle size is too small, it is easy to rub against the powder feeding equipment during the laser cladding process, causing blockage. Therefore, the particle size range of the high carbide content intermetallic compound alloy powder of this invention is controlled to be 74μm to 105μm.

[0045] The present invention also provides a cladding layer with high carbide content, which is prepared using the above-mentioned intermetallic compound alloy powder with high carbide content.

[0046] The present invention also provides a method for preparing a cladding layer with high carbide content, comprising the following steps:

[0047] Step 1: The above-mentioned intermetallic compound alloy powder with high carbide content is conveyed to the surface of the steel material using a coaxial powder feeding method;

[0048] Step 2: Using laser cladding, intermetallic compound alloy powder with high carbide content is clad onto the surface of steel material to form an in-situ self-generated carbide reinforced alloy cladding layer.

[0049] Specifically, in step 1 above, considering that when the powder feed rate is low, the dilution rate of the substrate (e.g., steel material) is high, and the hardness and wear resistance of the cladding layer decrease significantly; when the powder feed rate is high, the dilution rate of the substrate is low, the metallurgical bonding between the cladding layer and the substrate is insufficient, and unmelted powder may also appear. Therefore, the coaxial powder feed rate is controlled at 10g / min to 20g / min, for example, 15g / min to 20g / min.

[0050] Specifically, in step 2 above, considering the high carbide content in the intermetallic compound alloy powder of the present invention, if the laser cladding power is too low or the scanning speed is too high, some powder will not melt completely, resulting in unmelted material in the cladding layer and poor adhesion between the cladding layer and the substrate. Therefore, after in-depth research, the inventors controlled the laser cladding power to be 1800W to 2600W and the scanning speed to be 0.13m / min to 0.30m / min.

[0051] Specifically, in step 2 above, in the laser cladding method, the laser beam is a circular spot or a rectangular spot; when the laser beam is a circular spot, the diameter of the circular spot is 2 to 5 mm; when the laser beam is a rectangular spot, the length of the rectangular spot is 4 to 12 mm and the width is 2 to 5 mm.

[0052] Preferably, in step 2 above, the power of laser cladding is 2200-2400W and the scanning speed is 0.13-0.17m / min.

[0053] It should be noted that when using laser cladding technology to prepare the cladding layer, Cr7C3 melts and then re-forms in situ, which can reduce the size of Cr7C3 and make Cr7C3 more evenly distributed in the alloy coating.

[0054] Specifically, the thickness of the aforementioned cladding layer with high carbide content is 1.5 mm to 2.1 mm.

[0055] Specifically, the microstructure of the aforementioned high-carbide-content cladding layer consists of Ni3Al phase, γ-Ni phase, and carbides. The mass content of the γ-Ni phase is 3.0%–9.0%, and the carbides mainly include Cr7C3 carbides, with a mass content of 40%–50% and a carbide size of 2μm–5μm. The average hardness of the cladding layer is 800HV–1000HV (e.g., 850HV–1000HV), and the wear rate is ≤0.6×10⁻⁶. -5 mm 3 / (N·m).

[0056] Specifically, the cladding layer with high carbide content has a high bonding force with the substrate (metallurgical bonding), and the shear strength of the interface is 300-600 MPa. For example, the shear strength of the interface with the 42CrMo steel substrate is 500-600 MPa.

[0057] This invention also provides an application of the aforementioned high-carbide-content intermetallic compound alloy powder for surface modification of steel or nickel-based alloy components in heavy-duty diesel engines. This significantly improves the surface wear resistance of the steel or nickel-based alloy components in heavy-duty diesel engines.

[0058] The following detailed description of preferred embodiments of the present invention illustrates the principles of the invention and is not intended to limit the scope of the invention.

[0059] Example 1

[0060] This embodiment provides a high-carbide-content intermetallic compound alloy powder, a cladding layer, and a method for preparing the same.

[0061] The high-carbide-content intermetallic compound alloy powder in this embodiment was prepared by vacuum induction melting-inert gas atomization method. The morphology of the high-carbide-content intermetallic compound alloy powder is as follows: Figure 1 As shown, the particle size range of intermetallic compound alloy powder with high carbide content is 74 μm to 105 μm.

[0062] The chemical composition of the high carbide content intermetallic compound alloy powder of this embodiment, by mass percentage, is as follows: Al: 5.35%, C: 4.44%, Cr: 44.89%, B: 0.031%, O: 165ppm, N: 35ppm, H: 3.5ppm, with the balance being Ni; the atomic ratio of nickel equivalent to aluminum equivalent in the alloy powder is approximately 3.5; and the carbide content in the alloy powder is approximately 47%.

[0063] The above-mentioned intermetallic compound alloy powder with high carbide content was used to perform laser cladding on the surface of 45 steel. The laser power was 2200W, the scanning speed was 0.13m / min, the laser rectangular spot size was 5×2mm, and the coaxial powder feed rate was 20g / min, forming an in-situ self-generated carbide reinforced alloy cladding layer.

[0064] Figure 2 This is a morphology image of the cladding layer prepared in this embodiment. Figure 3 This is a microstructure diagram of the cladding layer prepared in this embodiment, by... Figure 2 As can be seen, the cladding layer in this embodiment has no cracks; Figure 3 As can be seen, the cladding layer in this embodiment has a microstructure consisting of Ni3Al phase, γ-Ni phase, and carbides. The carbides mainly include Cr7C3, with a carbide content of approximately 45%, and the γ-Ni phase has a mass content of approximately 6.7%. The carbides in the cladding layer of this embodiment are uniformly distributed, and the morphology of the carbides is a diffusely distributed granular form.

[0065] The thickness of the cladding layer in this embodiment is approximately 1.8 mm.

[0066] The average hardness of the cladding layer in this embodiment is 910 HV, and the shear strength of the interface between the cladding layer and the substrate is 352 MPa. Under dry friction conditions (surface friction, with gray cast iron as the grinding material), the wear rate of the cladding layer is 0.16 × 10⁻⁶. -5 mm 3 / (N·m).

[0067] Example 2

[0068] This embodiment provides a high-carbide-content intermetallic compound alloy powder, a cladding layer, and a method for preparing the same.

[0069] The high carbide content intermetallic compound alloy powder in this embodiment was prepared by vacuum induction melting-inert gas atomization method, and the particle size range of the high carbide content intermetallic compound alloy powder was 74 μm to 105 μm.

[0070] The chemical composition of the high carbide content intermetallic compound alloy powder of this embodiment, by mass percentage, is as follows: Al: 5.53%, C: 4.23%, Cr: 45.27%, B: 0.025%, O: 188ppm, N: 30ppm, H: 4ppm, with the balance being Ni; the atomic ratio of nickel equivalent to aluminum equivalent in the alloy powder is approximately 3.2; and the carbide content in the alloy powder is approximately 45%.

[0071] Laser cladding was performed on the surface of 42CrMo using the aforementioned intermetallic compound alloy powder with high carbide content. The laser power was 2400W, the scanning speed was 0.17m / min, the diameter of the laser circular spot was 3mm, and the coaxial powder feed rate was 15g / min, forming an in-situ self-generated carbide reinforced alloy cladding layer.

[0072] The cladding layer in this embodiment is free of cracks. The microstructure of the cladding layer consists of Ni3Al phase, γ-Ni phase, and carbides. The carbides mainly include Cr7C3, with a carbide content of approximately 44%, and the γ-Ni phase has a mass content of approximately 3.0%. The carbides in the cladding layer of this embodiment are uniformly distributed and exhibit a granular morphology.

[0073] The thickness of the cladding layer in this embodiment is approximately 2.0 mm.

[0074] The average hardness of the cladding layer in this embodiment is 865 HV, and the shear strength of the interface between the cladding layer and the substrate is 537 MPa. Under dry friction conditions (surface friction, with G15 steel as the grinding material), the wear rate of the laser cladding layer is 0.48 × 10⁻⁶. -5 mm 3 / (N·m).

[0075] Example 3

[0076] This embodiment provides a high-carbide-content intermetallic compound alloy powder, a cladding layer, and a method for preparing the same.

[0077] The high carbide content intermetallic compound alloy powder in this embodiment was prepared by vacuum induction melting-inert gas atomization method, and the particle size range of the high carbide content intermetallic compound alloy powder was 74 μm to 105 μm.

[0078] The chemical composition of the high carbide content intermetallic compound alloy powder of this embodiment, by mass percentage, is as follows: Al: 5.47%, C: 4.51%, Cr: 45.41%, B: 0.035%, O: 172ppm, N: 41ppm, H: 4ppm, with the balance being Ni; the atomic ratio of nickel equivalent to aluminum equivalent in the alloy powder is approximately 3.3; and the carbide content in the alloy powder is approximately 48%.

[0079] Laser cladding was performed on the surface of stainless steel using the aforementioned intermetallic compound alloy powder with high carbide content. The laser power was 2400W, the scanning speed was 0.12m / min, the laser rectangular spot size was 5×5mm, and the coaxial powder feed rate was 20g / min, forming an in-situ self-generated carbide reinforced alloy cladding layer.

[0080] The cladding layer in this embodiment is free of cracks. The microstructure of the cladding layer consists of Ni3Al phase, γ-Ni phase, and carbides. The carbides mainly include Cr7C3, with a carbide content of approximately 47% and a γ-Ni phase mass content of approximately 4.1%. The carbides in the cladding layer of this embodiment are uniformly distributed and exhibit a granular morphology.

[0081] The thickness of the cladding layer in this embodiment is 1.6 mm.

[0082] The average hardness of the cladding layer in this embodiment is 973 HV, and the shear strength of the interface between the cladding layer and the substrate is 339 MPa. Under dry friction conditions (point friction, with oxide ceramic as the grinding material), the wear rate of the laser cladding layer is 0.37 × 10⁻⁶. -5 mm 3 / (N·m).

[0083] Comparative Example 1

[0084] This comparative example provides an intermetallic compound alloy powder with high carbide content, a cladding layer, and a method for preparing the same.

[0085] The high-carbide-content intermetallic compound alloy powder of this comparative example was prepared by vacuum induction melting-inert gas atomization method, and the particle size range of the high-carbide-content intermetallic compound alloy powder was 74 μm to 105 μm.

[0086] The chemical composition of the high carbide content intermetallic compound alloy powder of this comparative example, by mass percentage, is as follows: Al: 5.49%, C: 4.25%, Cr: 45.41%, B: 0.023%, O: 162ppm, N: 33ppm, H: 4ppm, with the balance being Ni; the atomic ratio of nickel equivalent to aluminum equivalent in the alloy powder is approximately 3; the carbide content in the alloy powder is approximately 45%.

[0087] Laser cladding was performed on the surface of 42CrMo using the aforementioned intermetallic compound alloy powder with high carbide content. The laser power was 2400W, the scanning speed was 0.17m / min, the diameter of the laser circular spot was 3mm, and the coaxial powder feed rate was 15g / min, forming an in-situ self-generated carbide reinforced alloy cladding layer.

[0088] The nickel and aluminum equivalents in this comparative example have relatively low atomic numbers, and the cladding layer has cracks.

[0089] Comparative Example 2

[0090] This comparative example provides an intermetallic compound alloy powder with high carbide content, a cladding layer, and a method for preparing the same.

[0091] The high-carbide-content intermetallic compound alloy powder of this comparative example was prepared by vacuum induction melting-inert gas atomization method, and the particle size range of the high-carbide-content intermetallic compound alloy powder was 74 μm to 105 μm.

[0092] The chemical composition of the high carbide content intermetallic compound alloy powder in this comparative example is the same as that in Example 1, by mass percentage.

[0093] The above-mentioned intermetallic compound alloy powder with high carbide content was used to perform laser cladding on the surface of 45 steel. The laser power was 1600W, the scanning speed was 0.13m / min, the laser rectangular spot size was 5×2mm, and the coaxial powder feed rate was 20g / min, forming an in-situ self-generated carbide reinforced alloy cladding layer.

[0094] In this comparative example, the cladding layer contained unmelted powder, the bonding force between the cladding layer and the substrate was low, and the shear strength of the interface between the cladding layer and the substrate was 187 MPa.

[0095] Comparative Example 3

[0096] This comparative example provides an intermetallic compound alloy powder, a cladding layer, and a method for preparing the same.

[0097] In this comparative example, Ni3Al / carbide composite powder was prepared by vacuum induction melting-inert gas atomization method, and the particle size range of the powder was 53μm to 124μm.

[0098] The chemical composition of the Ni3Al / carbide composite powder, by mass percentage, is as follows: Al: 9.22%, C: 1.35%, Cr: 19.01%, B: 0.06%, O: 146ppm, N: 25ppm, H: 3ppm, with the balance being Ni. The atomic ratio of nickel equivalent to aluminum equivalent is approximately 3, and the mass content of in-situ self-generated carbides is approximately 16.5%.

[0099] The above-mentioned Ni3Al / carbide composite powder was used to perform laser cladding on the surface of 42CrMo steel. The laser power was 2000W, the scanning speed was 0.18m / min, the laser rectangular spot size was 5mm×2mm, and the coaxial powder feed rate was 17.5g / min, forming an in-situ self-generated carbide reinforced Ni3Al-based alloy cladding layer.

[0100] The in-situ self-generated carbide-reinforced Ni3Al-based alloy cladding layer prepared in this comparative example was crack-free and exhibited uniform carbide distribution. However, the average hardness of the Ni3Al-based alloy reinforced layer was relatively low, at 546 HV. Under dry friction conditions (surface friction, with gray cast iron as the grinding material), the wear rate of the Ni3Al-based alloy reinforced layer was 1.19 × 10⁻⁶. -5 mm 3The wear rate of the grinding material, gray cast iron, is 3.05 × 10⁻⁶ N·m. -5 mm 3 / (N·m).

[0101] Compared with Example 1, the cladding layer of this comparative example has lower hardness and wear resistance.

[0102] The above description is only a preferred embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any changes or substitutions that can be easily conceived by those skilled in the art within the scope of the technology disclosed in the present invention should be included within the scope of protection of the present invention.

Claims

1. An intermetallic alloy powder with high carbide content, characterized in that, The high-carbide-content intermetallic compound alloy powder has a chemical composition in mass percentage of Al 5.0%-5.8%, C 4.1%-4.6%, Cr 44.0%-46.0%, B 0.02%-0.04%, O≤200ppm, N≤50ppm, H≤10ppm, and the balance of Ni; The atomic number ratio of the nickel equivalent and the aluminum equivalent in the high-carbide-content intermetallic compound alloy powder is 3.2-3.7; The calculation principle of the atomic number of the nickel equivalent is: wherein Ni represents the mass percentage of Ni element in the intermetallic compound alloy powder with high carbide content, Cr Ni3Al溶 is 3% to 7%; The calculation principle of the atomic number of the aluminum equivalent is: wherein Al represents the mass percentage of the Al element in the high-carbide-content intermetallic compound alloy powder; The microstructure of the high-carbide-content intermetallic compound alloy powder comprises a Ni3Al phase, a γ-Ni phase, and carbides, and the carbide structure mainly comprises Cr7C3, the mass content of the carbides is 45%-50%, and the mass content of the γ-Ni phase is 3.0%-9.0%; The average hardness of the cladding layer prepared by using the high-carbide-content intermetallic compound alloy powder is 850HV-1000HV.

2. The intermetallic alloy powder with high carbide content according to claim 1, characterized in that, The mass content of the carbides is 45%-47%.

3. The high carbide content intermetallic alloy powder of claim 1, wherein, The atomic number ratio of the nickel equivalent and the aluminum equivalent in the high-carbide-content intermetallic compound alloy powder is 3.2-3.

5.

4. The high carbide content intermetallic alloy powder of claim 1, wherein, The high-carbide-content intermetallic compound alloy powder has a chemical composition in mass percentage of Al 5.3%-5.7%, C 4.2%-4.6%, Cr 44.5%-46.0%, B 0.02%-0.038%, O≤190ppm, N≤45ppm, H≤7ppm, and the balance of Ni.

5. A high carbide content cladding layer characterized by, The cladding layer is prepared by using the high-carbide-content intermetallic compound alloy powder according to any one of claims 1-4.

6. A method of producing a high-carbide-content cladding layer as claimed in claim 5, characterized in that The method comprises the following steps: Step 1: delivering the high-carbide-content intermetallic compound alloy powder to the surface of a steel material by using a coaxial powder delivery method; Step 2: cladding the high-carbide-content intermetallic compound alloy powder on the surface of the steel material by using a laser cladding method to form a cladding layer.

7. The preparation method according to claim 6, characterized in that, In the step 1, the coaxial powder delivery amount is controlled to be 10g / min-20g / min.

8. The preparation method according to claim 6, characterized in that, In the step 2, the laser cladding power is controlled to be 1800W-2600W, and the scanning speed is controlled to be 0.13m / min-0.30m / min.

9. The production method according to any one of claims 6 to 8, characterized in that, The average hardness of the cladding layer is 800-1000 HV, and the wear rate is ≤0.6*10 -5 mm 3 / (N·m).

10. Use of an intermetallic alloy powder with a high carbide content, characterized in that The high-carbide-content intermetallic compound alloy powder according to any one of claims 1-4 is used for surface modification of a steel or nickel-based alloy component of a heavy-duty diesel engine.

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