CN115011843A - In-situ authigenic carbide reinforced Ni3 Al-based alloy powder and laser cladding method and application thereof - Google Patents
In-situ authigenic carbide reinforced Ni3 Al-based alloy powder and laser cladding method and application thereof Download PDFInfo
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- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
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- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
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- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
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Abstract
The invention provides an in-situ autocarbide reinforced Ni 3 Al-based alloy powder and a laser cladding method and application thereof, relating to the technical field of laser processing materials. The in-situ authigenic carbide provided by the invention enhances Ni 3 The Al-based alloy powder comprises the following chemical components in percentage by mass: 7.8-9.3% of Al, 1.7-2.2% of C, 22.5-26% of Cr, 0.02-0.08% of B, less than or equal to 200ppm of O, less than or equal to 50ppm of N, less than or equal to 10ppm of H and the balance of Ni; the Ni 3 The in-situ authigenic carbide of the Al-base alloy powder is Cr 7 C 3 ，Cr 7 C 3 The mass content of (A) is 22-28%. By using Ni provided by the invention 3 Alloy prepared from Al-based alloy powderThe gold coating has compact structure, high bonding strength with the matrix and good wear resistance.
Description
Technical Field
The invention relates to the technical field of laser processing materials, in particular to in-situ authigenic carbide reinforced Ni 3 Al-based alloy powder and a laser cladding method and application thereof.
Background
The heavy-load high-power diesel engine is core power equipment of large ships and locomotives, and is widely applied to the field of energy equipment such as power stations, land generator sets and the like. As the 'heart' of the diesel engine, the piston assembly is the most severe assembly in the whole internal combustion engine system, the energy loss caused by friction and heat dissipation accounts for more than 60% of the whole internal combustion engine, and therefore the performance of the piston assembly directly influences the output power and the service cycle of the diesel engine. In recent years, with the emergence of stringent Tier IV, european VI, national six and other emission regulations and the gradual increase of fuel economy and high power requirements, heavy-duty diesel engines are developing towards high mechanical load, high thermal load and low emission, and the internal working environment is becoming worse. The severer working environment puts high requirements on the surface wear performance of the piston assembly, and the existing piston assembly material structure, coating material system and coating technology have great limitations. Therefore, the research and development of a novel coating material system and a preparation technology thereof, and the improvement of the quality and the performance of the piston assembly become key technical problems which need to be overcome urgently by research and application units of domestic and foreign diesel engines.
Chinese patent 201410822105.5 provides a method for preparing Ni with compact structure, high bonding strength with a matrix and good wear resistance by using laser cladding technology 3 Al/Cr 3 C 2 The method for compounding the coating has good application prospect in the field of heavy-duty high-power diesel engines. However, this technique employs Ni 3 Al alloy powder and Cr 3 C 2 When the mixture of the powder is used as cladding powder, the problems of cracks and uneven carbide distribution are easy to occur, and Ni is seriously influenced 3 Al/Cr 3 C 2 Engineering application of the composite coating.
Disclosure of Invention
The invention aims to provide in-situ authigenic carbide reinforced Ni 3 Al-based alloy powder, application thereof and in-situ autocarbide reinforced Ni 3 A preparation method of an Al-based alloy coating. The in-situ authigenic carbide provided by the invention enhances Ni 3 Al-based alloy powder capable of solving existing Ni 3 Al/Cr 3 C 2 The laser cladding layer has the problems of large crack tendency and uneven carbide distribution, and meets the requirement of the surface wear resistance of key parts of the heavy-duty high-power diesel engine.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides an in-situ autocarbide reinforced Ni 3 The Al-based alloy powder comprises the following chemical components in percentage by mass: 7.8-9.3% of Al, 1.7-2.2% of C, 22.5-26% of Cr, 0.02-0.08% of B, less than or equal to 200ppm of O, less than or equal to 50ppm of N, less than or equal to 10ppm of H, and the balance of Ni;
the Ni 3 The in-situ authigenic carbide of the Al-based alloy powder is Cr 7 C 3 ，Cr 7 C 3 The mass content of (A) is 22-28%.
Preferably, the Ni 3 The Al-based alloy powder is prepared by a plasma rotating electrode method or a vacuum induction melting-inert gas atomization method.
Preferably, the Ni 3 The particle size range of the Al-based alloy powder is 45-125 mu m.
The invention provides the Ni in the technical scheme 3 The Al-based alloy powder is applied to heavy-duty diesel engines.
The invention provides an in-situ autocarbide reinforced Ni 3 The laser cladding method of the Al-based alloy powder comprises the following steps:
the Ni in the technical scheme is prepared by using a laser cladding technology 3 Al-based alloy powder is cladded on the surface of the steel material to form in-situ authigenic carbide reinforced Ni 3 An Al-based alloy coating.
Preferably, coaxialFeeding the Ni powder or paraxially feeding the Ni powder 3 Conveying the Al-based alloy powder to the surface of the steel material; the powder feeding amount of the coaxial powder feeding or the paraxial powder feeding is 5-35 g/min.
Preferably, the laser cladding power is 1200-3500W, the scanning speed is 0.12-0.60 m/min, and the laser beam is a circular spot or a rectangular spot; when the laser beam is a circular light spot, the diameter of the circular light spot is 2-5 mm; when the laser beam is a rectangular light spot, the length of the rectangular light spot is 5-30 mm, and the width of the rectangular light spot is 1-10 mm.
Preferably, the laser adopted by the laser cladding is fiber laser, disc laser, CO 2 Laser, Nd is YAG laser or semiconductor laser.
Preferably, the steel material is one of carbon steel, alloy steel, heat-resistant stainless steel, and cast iron.
Preferably, the in-situ autocarbide strengthens Ni 3 The thickness of the Al-based alloy coating is 0.3-2.5 mm, the average hardness is more than or equal to 550HV, and the wear rate is less than or equal to 1.0 multiplied by 10 -5 mm 3 N.m, and the friction coefficient is less than or equal to 0.6.
The invention provides an in-situ autocarbide reinforced Ni 3 Al-based alloy powder, in the present invention, Cr 7 C 3 Distributed in Ni in an in-situ self-generated manner 3 In the Al-based alloy powder, Cr can be increased 7 C 3 Uniformity of distribution in the alloy powder; when the laser cladding technology is adopted to prepare the alloy coating, Cr 7 C 3 Is formed in situ again after melting, and can reduce Cr 7 C 3 Size of Cr 7 C 3 The distribution in the alloy coating is more uniform. The in-situ authigenic carbide provided by the invention is adopted to reinforce Ni 3 The alloy coating prepared from the Al-based alloy powder has a compact structure, high bonding strength with a matrix and good wear resistance. Solves the existing Ni 3 Al/Cr 3 C 2 The laser cladding layer has the problems of large crack tendency and uneven carbide distribution, and can meet the requirement of the surface wear resistance of key parts of heavy-duty high-power diesel engines.
Drawings
FIG. 1 is a crude prepared in example 1Enhanced Ni by autobiogenic carbide 3 A morphology of the Al-based alloy powder;
FIG. 2 is the in situ autocarbide enhanced Ni prepared in example 2 3 A morphology map of the Al-based alloy powder;
FIG. 3 shows in-situ autocarbide strengthened Ni prepared in example 1 3 The texture and morphology of the Al-based alloy powder;
FIG. 4 shows in-situ autocarbide strengthened Ni prepared in example 1 3 A topography of the Al-based alloy coating;
FIG. 5 is a topographical view of the region 1 of FIG. 4;
FIG. 6 is a topographical view of the region 2 of FIG. 4;
FIG. 7 shows Ni prepared in comparative example 1 3 Al/Cr 3 C 2 A composite cladding layer topography;
FIG. 8 is a topographical view of the region 3 of FIG. 7;
FIG. 9 is a topographical view of the region 4 of FIG. 7;
FIG. 10 is a topographical view of the region 5 of FIG. 7;
FIG. 11 is a topographical view of the region 6 of FIG. 7.
Detailed Description
The invention provides an in-situ autocarbide reinforced Ni 3 The Al-based alloy powder comprises the following chemical components in percentage by mass: 7.8-9.3% of Al, 1.7-2.2% of C, 22.5-26% of Cr, 0.02-0.08% of B, less than or equal to 200ppm of O, less than or equal to 50ppm of N, less than or equal to 10ppm of H, and the balance of Ni;
the Ni 3 The in-situ authigenic carbide of the Al-based alloy powder is Cr 7 C 3 ，Cr 7 C 3 The mass content of (A) is 22-28%.
In the present invention, the Ni is present in mass percent 3 The chemical composition of the Al-based alloy powder comprises 7.8-9.3% of Al, and preferably 8.06-8.79%.
In the present invention, the Ni is present in mass percent 3 The chemical composition of the Al-based alloy powder comprises 1.7-2.2% of C, preferably 1.87-2.16%.
In the invention, the weight percentage isNi as described above 3 The chemical composition of the Al-based alloy powder comprises 22.5-26% of Cr, and preferably 22.82-25.90%.
In the present invention, the Ni is present in mass percent 3 The chemical composition of the Al-based alloy powder comprises 0.02-0.08% of B, preferably 0.023-0.040%.
In the present invention, the Ni is present in mass percent 3 The chemical composition of the Al-based alloy powder comprises O less than or equal to 200 ppm.
In the present invention, the Ni is, in mass percent 3 The chemical composition of the Al-based alloy powder comprises N less than or equal to 50 ppm.
In the present invention, the Ni is present in mass percent 3 The chemical composition of the Al-based alloy powder comprises H less than or equal to 10 ppm.
In the present invention, the Ni 3 The chemical composition of the Al-based alloy powder includes the balance Ni.
In the present invention, the Ni 3 The in-situ authigenic carbide of the Al-base alloy powder is Cr 7 C 3 ，Cr 7 C 3 The content of (b) is preferably 22 to 28% by mass, more preferably 24 to 25% by mass.
In the present invention, the Ni 3 The Al-based alloy powder is preferably prepared by a plasma rotating electrode method or a vacuum induction melting-inert gas atomization method.
In the present invention, the Ni 3 The grain size range of the Al-based alloy powder is preferably 45-125 mu m.
The invention also provides Ni in the technical scheme 3 The application of the Al-based alloy powder in heavy-duty diesel engines is preferably applied to the preparation of surface coatings of piston components.
The invention also provides in-situ autocarbide reinforced Ni 3 The laser cladding method of the Al-based alloy powder comprises the following steps:
the Ni in the technical scheme is prepared by using a laser cladding technology 3 Al-based alloy powder is cladded on the surface of the steel material to form in-situ authigenic carbide reinforced Ni 3 An Al-based alloy coating.
In the present invention, the use of laser lightCladding technology adopts the technical scheme of Ni 3 The step of cladding the Al-based alloy powder on the surface of the ferrous material preferably includes: providing the surface of a ferrous material with the Ni 3 Al-based alloy powder and simultaneously carrying out laser scanning on the surface of the steel material.
In the present invention, the steel material is preferably one of carbon steel, alloy steel, heat-resistant stainless steel, and cast iron.
The invention preferably adopts a mode of coaxially feeding powder or paraxially feeding powder to feed the Ni 3 Conveying the Al-based alloy powder to the surface of the steel material; the powder feeding amount of the coaxial powder feeding or the paraxial powder feeding is preferably 5-35 g/min, and more preferably 10-25 g/min.
In the invention, the laser cladding power is preferably 1200-3500W, more preferably 1500-2200W; the scanning speed is preferably 0.12-0.60 m/min, and more preferably 0.18-0.30 m/min; the laser beam is preferably a circular spot or a rectangular spot; when the laser beam is a circular light spot, the diameter of the circular light spot is preferably 2-5 mm, and more preferably 3-4 mm; when the laser beam is a rectangular light spot, the length of the rectangular light spot is preferably 5-30 mm, more preferably 10-20 mm, and the width of the rectangular light spot is preferably 1-10 mm, more preferably 2-5 mm.
In the invention, the laser adopted by the laser cladding is preferably fiber laser, disc laser and CO 2 Laser, Nd is YAG laser or semiconductor laser. In the invention, the protective gas adopted by laser cladding is preferably argon, and the flow of the protective gas is preferably 10-30L/min, and more preferably 15-20L/min;
in the present invention, the in-situ autocarbide reinforces Ni 3 The thickness of the Al-based alloy coating is preferably 0.3-2.5 mm; the average hardness is preferably more than or equal to 550 HV; the wear rate is preferably less than or equal to 1.0X 10 -5 mm 3 V (N · m); the coefficient of friction is preferably ≦ 0.6.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
In-situ authigenic carbide reinforced Ni prepared by plasma rotating electrode method 3 The morphology of the Al-based alloy powder is shown in FIG. 1, Ni 3 The particle size of the Al-based alloy powder is 45-125 μm.
By mass percent, Ni 3 The Al-based alloy powder comprises the following chemical components: 8.63 percent of Al, 2.16 percent of C, 25.90 percent of Cr, 0.035 percent of B, 40ppm of O, 27ppm of N, 3ppm of H and the balance of Ni and Ni 3 The Al-based alloy powder had a structure in which Cr carbide was in-situ synthesized as shown in FIG. 3 7 C 3 The mass content of (A) is 25%.
Using the above-mentioned Ni 3 Carrying out laser cladding on the surface of 42CrMo steel by using Al-based alloy powder, wherein the laser cladding uses fiber laser, the laser power is 2000W, the scanning speed is 0.18m/min, the rectangular laser spot size is 5mm multiplied by 2mm, the coaxial powder feeding amount is 17.5g/min, the protective gas adopted by the laser cladding is argon, the flow of the argon is 15L/min, and the in-situ authigenic carbide reinforced Ni is formed 3 An Al-based alloy coating.
In-situ autocarbide reinforced Ni prepared in this example 3 The morphology of the Al-based alloy coating is shown in figures 4-6, the obtained coating has no cracks, the carbide is uniformly distributed, the thickness of the coating is 2.2mm, and the average hardness is 600 HV. In-situ autobiogenic carbide reinforced Ni under dry friction conditions (surface friction, with the opposite abrasive material being gray cast iron) 3 The wear rate of the Al-based alloy coating is 0.26 multiplied by 10 -5 mm 3 /(N.m), the wear rate on the abrasive gray cast iron was 0.35X 10 -5 mm 3 V (N.m), the coefficient of friction was 0.39.
Comparative example 1
By using Ni 3 Al alloy powder and Cr 3 C 2 Mixture of powders as cladding powder Ni prepared with the same laser cladding parameters as example 1 3 Al/Cr 3 C 2 The appearance of the composite cladding layer is shown in figures 7-11, the obtained cladding layer has cracks, the carbide is not uniformly distributed, and the average hardness of the cladding layer is550HV。
Ni Using the same test method as in example 1 3 Al/Cr 3 C 2 The laser cladding layer formed by the mixed powder had a wear rate of 0.31X 10 -5 mm 3 /(N.m), the wear rate on the abrasive gray cast iron was 0.76X 10 -5 mm 3 V (N · m), the coefficient of friction was 0.58.
As is clear from comparison between example 1 and comparative example 1, Ni was reinforced with the in-situ autocarbide of the present invention 3 The Al-based alloy powder and the cladding layer obtained by the laser cladding method have good wear resistance, no crack on the cladding layer and uniform carbide distribution.
Example 2
In-situ authigenic carbide reinforced Ni prepared by vacuum induction melting-inert gas atomization method 3 The morphology of the Al-based alloy powder is shown in FIG. 2, Ni 3 The particle size of the Al-based alloy powder is 45-125 μm.
By mass percent, Ni 3 The Al-based alloy powder comprises the following chemical components: 8.79 percent of Al, 2.01 percent of C, 24.18 percent of Cr, 0.023 percent of B, 195ppm of O, 32ppm of N, 4.5ppm of H and the balance of Ni, and in-situ synthesized carbide Cr 7 C 3 The mass content of (A) is 24%.
Using the above Ni 3 Performing laser cladding on the surface of the vermicular graphite cast iron by using Al-based alloy powder, wherein the laser cladding uses optical fiber laser, the laser power is 1500W, the scanning speed is 0.30m/min, the diameter of a laser circular light spot is 3mm, the coaxial powder feeding amount is 10g/min, the protective gas adopted by the laser cladding is argon, the flow of the argon is 10L/min, and the in-situ authigenic carbide reinforced Ni is formed 3 An Al-based alloy coating.
In-situ autogrown carbide reinforced Ni prepared in this example 3 The Al-based alloy coating has no cracks, the carbide is uniformly distributed, the thickness of the coating is 1.1mm, and the average hardness is 580 HV. In-situ autobiogenic carbide reinforced Ni under dry friction conditions (surface friction, with the opposite abrasive material being gray cast iron) 3 The wear rate of the Al-based alloy coating is 0.37 multiplied by 10 -5 mm 3 /(N.m), wear rate to grey cast iron as abrasive material 0.52X 10 -5 mm 3 V (N.m), coefficient of friction 0.45。
Example 3
In-situ authigenic carbide reinforced Ni prepared by vacuum induction melting-inert gas atomization method 3 The particle size of the Al-based alloy powder is 45-125 μm.
By mass percent, Ni 3 The Al-based alloy powder comprises the following chemical components: 8.06% of Al, 1.87% of C, 22.82% of Cr, 0.028% of B, 159ppm of O, 31ppm of N, 4ppm of H and the balance of Ni, and in-situ authigenic carbide Cr 7 C 3 The mass content of (A) is 24%.
Using the above-mentioned Ni 3 Performing laser cladding on the surface of 45# steel by using Al-based alloy powder, wherein the laser cladding uses fiber laser, the laser power is 2200W, the scanning speed is 0.18m/min, the rectangular laser spot size is 5mm multiplied by 2mm, the coaxial powder feeding amount is 20g/min, the protective gas adopted by the laser cladding is argon, the flow of the argon is 15L/min, and the in-situ authigenic carbide reinforced Ni is formed 3 An Al-based alloy coating.
In-situ autocarbide reinforced Ni prepared in this example 3 The Al-based alloy coating has no cracks, the carbide is uniformly distributed, the thickness of the coating is 1.1mm, and the average hardness is 610 HV. In-situ autobiogenic carbide reinforced Ni under dry friction conditions (surface friction, with the opposite abrasive material being gray cast iron) 3 The wear rate of the Al-based alloy coating is 0.43X 10 -5 mm 3 /(N.m), wear rate to grey cast iron as abrasive material 0.68X 10 -5 mm 3 V (N.m), the coefficient of friction was 0.49.
Example 4
In-situ authigenic carbide reinforced Ni prepared by vacuum induction melting-inert gas atomization method 3 The particle size of the Al-based alloy powder is 45-125 μm.
By mass percent, Ni 3 The Al-based alloy powder comprises the following chemical components: 8.58 percent of Al, 1.92 percent of C, 24.35 percent of Cr, 0.040 percent of B, 181ppm of O, 38ppm of N, 4ppm of H and the balance of Ni, and in-situ synthesized carbide Cr 7 C 3 The mass content of (A) is 25%.
Using the above-mentioned Ni 3 Performing laser cladding on the surface of 4Cr14Ni14W2Mo steel by using Al-based alloy powder, wherein the laser cladding uses semiconductor laserThe laser power is 3500W, the scanning speed is 0.12m/min, the laser rectangular spot size is 20mm multiplied by 2mm, the paraxial powder feeding amount is 25g/min, the protective gas adopted by laser cladding is argon, the flow of the argon is 30L/min, and the in-situ authigenic carbide reinforced Ni is formed 3 An Al-based alloy coating.
In-situ autocarbide reinforced Ni prepared in this example 3 The Al-based alloy coating has no cracks, the carbide is uniformly distributed, the thickness of the coating is 1.8mm, and the average hardness is 560 HV. Under the condition of dry friction (surface friction, the opposite-grinding material is gray cast iron), the in-situ authigenic carbide strengthens Ni 3 The wear rate of the Al-based alloy coating is 0.65 multiplied by 10 -5 mm 3 /(N.m), the wear rate on the abrasive gray cast iron was 0.97X 10 -5 mm 3 V (N.m), the coefficient of friction was 0.56.
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.
Claims (10)
1. In-situ authigenic carbide reinforced Ni 3 The Al-based alloy powder is characterized by comprising the following chemical components in percentage by mass: 7.8-9.3% of Al, 1.7-2.2% of C, 22.5-26% of Cr, 0.02-0.08% of B, less than or equal to 200ppm of O, less than or equal to 50ppm of N, less than or equal to 10ppm of H and the balance of Ni;
the Ni 3 The in-situ authigenic carbide of the Al-based alloy powder is Cr 7 C 3 ，Cr 7 C 3 The mass content of (A) is 22-28%.
2. Ni according to claim 1 3 Al-based alloy powder, characterized in that said Ni 3 The Al-based alloy powder is prepared by a plasma rotating electrode method or a vacuum induction melting-inert gas atomization method.
3. Ni according to claim 1 3 Al-based alloy powder, characterized in that said Ni 3 The particle size range of the Al-based alloy powder is 45-125 mu m.
4. Ni as defined in any one of claims 1 to 3 3 The Al-based alloy powder is applied to heavy-duty diesel engines.
5. In-situ authigenic carbide reinforced Ni 3 The laser cladding method of the Al-based alloy powder comprises the following steps:
use of laser cladding technique to coat Ni as defined in any one of claims 1 to 3 3 Al-based alloy powder is cladded on the surface of a steel material to form in-situ authigenic carbide reinforced Ni 3 And (3) coating Al-based alloy.
6. Laser cladding method according to claim 5, wherein said Ni is fed by coaxial or paraxial feeding 3 Conveying the Al-based alloy powder to the surface of the steel material; the powder feeding amount of the coaxial powder feeding or the paraxial powder feeding is 5-35 g/min.
7. The laser cladding method of claim 5, wherein the laser cladding power is 1200-3500W, the scanning speed is 0.12-0.60 m/min, and the laser beam is a circular spot or a rectangular spot; when the laser beam is a circular light spot, the diameter of the circular light spot is 2-5 mm; when the laser beam is a rectangular light spot, the length of the rectangular light spot is 5-30 mm, and the width of the rectangular light spot is 1-10 mm.
8. The laser cladding method according to claim 5, wherein the laser adopted by the laser cladding is fiber laser, disc laser, CO 2 Laser, Nd is YAG laser or semiconductor laser.
9. Laser cladding method according to claim 5, wherein said steel material is one of carbon steel, alloy steel, heat resistant stainless steel and cast iron.
10. According to claim 5The laser cladding method is characterized in that the in-situ autocarbide reinforced Ni 3 The thickness of the Al-based alloy coating is 0.3-2.5 mm, the average hardness is more than or equal to 550HV, and the wear rate is less than or equal to 1.0 multiplied by 10 -5 mm 3 N.m, and the friction coefficient is less than or equal to 0.6.
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| CN115558924A (en) * | 2022-11-11 | 2023-01-03 | 阳江市安佳乐厨业有限公司 | Cutter for in-situ generation of carbide through laser cladding and preparation method thereof |
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