CN117721462A - Fe-based fine-grain laser cladding layer with high wear resistance on surface of spheroidal graphite cast iron and preparation method thereof - Google Patents
Fe-based fine-grain laser cladding layer with high wear resistance on surface of spheroidal graphite cast iron and preparation method thereof Download PDFInfo
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- CN117721462A CN117721462A CN202410050719.XA CN202410050719A CN117721462A CN 117721462 A CN117721462 A CN 117721462A CN 202410050719 A CN202410050719 A CN 202410050719A CN 117721462 A CN117721462 A CN 117721462A
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- cladding layer
- laser cladding
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- spheroidal graphite
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 47
- 229910001141 Ductile iron Inorganic materials 0.000 title claims abstract description 41
- 238000004372 laser cladding Methods 0.000 title claims abstract description 36
- 238000002360 preparation method Methods 0.000 title claims abstract description 8
- 239000000843 powder Substances 0.000 claims abstract description 76
- 238000005253 cladding Methods 0.000 claims abstract description 57
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 30
- 239000000956 alloy Substances 0.000 claims abstract description 30
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 claims abstract description 12
- 239000002245 particle Substances 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 13
- 239000000758 substrate Substances 0.000 claims description 12
- 229910000628 Ferrovanadium Inorganic materials 0.000 claims description 8
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 239000007789 gas Substances 0.000 claims description 6
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 230000001360 synchronised effect Effects 0.000 claims description 3
- 239000000463 material Substances 0.000 abstract description 12
- 239000013078 crystal Substances 0.000 abstract description 11
- 230000005496 eutectics Effects 0.000 abstract description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 10
- 238000011065 in-situ storage Methods 0.000 abstract description 9
- 230000007547 defect Effects 0.000 abstract description 7
- 229910002804 graphite Inorganic materials 0.000 abstract description 7
- 239000010439 graphite Substances 0.000 abstract description 7
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 238000005728 strengthening Methods 0.000 abstract description 4
- 238000005266 casting Methods 0.000 abstract description 3
- 229910000734 martensite Inorganic materials 0.000 abstract description 3
- 230000007704 transition Effects 0.000 abstract description 2
- 230000000052 comparative effect Effects 0.000 description 11
- 230000003287 optical effect Effects 0.000 description 6
- 238000005299 abrasion Methods 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 229910001018 Cast iron Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 239000003153 chemical reaction reagent Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000032798 delamination Effects 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 230000009471 action Effects 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 230000004075 alteration Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000005065 mining Methods 0.000 description 1
- 230000008439 repair process Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000004781 supercooling Methods 0.000 description 1
- 238000012876 topography Methods 0.000 description 1
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical group [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- Other Surface Treatments For Metallic Materials (AREA)
Abstract
The invention relates to the field of laser cladding surface strengthening and remanufacturing, and discloses a high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of a spheroidal graphite cast iron and a preparation method thereof. The alloy powder for laser cladding of the invention only consists of reduced iron powder and vanadium iron powder, has simple formula and easy manufacture, successfully obtains a large amount of in-situ self-generated VC by means of graphite reverse transition in the spheroidal graphite cast iron base material, and the cladding layer consists of martensite, a large amount of eutectic structures distributed among crystals and in-situ self-generated VC. The invention can greatly improve the surface hardness and wear resistance of the spheroidal graphite cast iron base material under the condition of adopting simpler alloy powder, and has lower cost of repairing or surface modifying the surface defects of the iron castings.
Description
Technical Field
The invention relates to the field of laser cladding surface strengthening and remanufacturing, in particular to a high-wear-resistance Fe-based fine-grain laser cladding layer on a nodular cast iron surface and a preparation method thereof.
Background
The spheroidal graphite cast iron has excellent wear resistance and impact resistance, can bear the requirements of high-pressure and high-temperature environments, and is widely used in various fields such as automobile manufacturing, mechanical manufacturing, pipeline systems, mining equipment and the like. However, with the rapid development of industry and the requirements of modern industry, ductile iron is more common in working under extreme environments, and serious abrasion and corrosion phenomena are often generated, so that workpieces are damaged and fail. The method has very important significance in repairing or modifying the surface defects of the iron castings so as to prolong the service life and widen the application range. At present, technologies such as arc spraying, electron beam welding, inert gas shielded welding and the like are mostly adopted in the industry to repair ductile cast iron workpieces. However, due to the high carbon content of spheroidal graphite cast iron, a hard brittle phase is easily generated at the interface region during welding and cladding, and the interfacial tensile strength is also reduced. During cooling, shrinkage of the weld and cladding layers also produces high residual stresses, resulting in cracking of the interface.
The laser cladding technology is a surface modification technology which is widely applied gradually, and can obtain a high-performance cladding layer which is metallurgically bonded with a substrate. Compared with other welding processes, the laser cladding technology has higher precision and controllability, higher efficiency and relatively lower heat input, so that the forming quality of the laser cladding technology is more controllable when repairing spheroidal graphite cast iron. The iron-based alloy powder is widely used because of low cost, excellent wear resistance, small residual stress generated by the similar components with the base material, and low cost.
Chinese patent publication No. CN115786907a discloses a laser cladding powder and a method for laser cladding on the surface of spheroidal graphite cast iron, the alloy powder used comprises: 30 to 65wt% of a first powder and 35 to 70wt% of a second powder. The first powder includes 0.01wt% to 0.05wt% of C, 1wt% to 3wt% of Cr, 1wt% to 2.5wt% of Si, 0.1wt% to 1wt% of Fe, 0.5wt% to 1.5wt% of B, 0.5wt% to 2wt% of Co, 15wt% to 30wt% of Cu, and the balance of Ni. The second powder is tungsten carbide powder. Although the cladding layer can reach higher hardness, the alloy powder has more complex formula, higher content of alloy elements and higher overall cost of the powder.
Disclosure of Invention
The invention aims to solve the technical problems that: provides a high wear-resistant Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron with low comprehensive cost and a preparation method of the high wear-resistant Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron.
In order to solve the technical problems, the preparation method of the Fe-based fine-grain laser cladding layer with high wear resistance on the surface of the spheroidal graphite cast iron comprises the step of preparing the cladding layer on the surface of a spheroidal graphite cast iron substrate by adopting a laser cladding method, wherein cladding alloy powder consists of reduced iron powder and ferrovanadium powder with certain proportion and unequal grain sizes.
Preferably, the alloy powder includes: 51.5wt.% reduced iron powder, 48.5wt.% vanadic iron powder.
Preferably, the alloy powder is variable-particle-size alloy powder, the particle size of the reduced iron powder ranges from 100 meshes to 200 meshes, and the particle size of the vanadium iron powder ranges from 400 meshes to 600 meshes. Because the reduced iron powder and the ferrovanadium powder adopt different particle size ranges, the waste alloy powder collected after laser cladding is easy to screen out the reduced iron powder and the ferrovanadium powder, and the recycled alloy powder can be reused.
Preferably, a synchronous powder feeding laser cladding mode is adopted, cladding alloy powder consists of reduced iron powder and ferrovanadium powder with certain proportion of unequal particle sizes, the laser power is 1000W, the pulse frequency is 4500Hz, the duty ratio is 95%, the light spot diameter is 2.0mm, the scanning speed is 12mm/s, the lap joint rate is 30%, the powder feeding amount is 6-7 g/min, the powder feeding gas flow is 4.5L/min, and the coaxial shielding gas argon flow is 16L/min.
Preferably, the alloy powder is mixed in a V-type powder mixer for 1.5-3 hours before laser cladding.
The Fe-based fine-grain laser cladding layer with high wear resistance on the surface of the spheroidal graphite cast iron is prepared by adopting the preparation method of any one of the Fe-based fine-grain laser cladding layers with high wear resistance on the surface of the spheroidal graphite cast iron.
The beneficial effects of the invention are as follows: the alloy powder for laser cladding is composed of reduced iron powder and ferrovanadium powder, has a simple formula and is easy to manufacture, and a cladding layer is composed of martensite, a large number of eutectic structures distributed among crystals and in-situ autogenous VC, wherein graphite in a ductile iron substrate is reversely transited by virtue of the graphite in the ductile iron substrate in cooperation with specific laser parameters, so that a large amount of in-situ autogenous VC is successfully obtained. Because carbon elements in the cladding layer are more consumed, generated cementite participates in eutectic reaction, and a large number of eutectic structures which are uniformly distributed are generated.
When the ductile iron base material is subjected to laser cladding surface strengthening and remanufacturing, a preheating slow cooling step is not needed, no obvious crack defect exists in the prepared cladding layer, the cladding layer consists of a large number of equiaxed crystals and a part of near equiaxed crystals, the average hardness of the cladding layer can reach 950HV0.2, the average hardness of the cladding layer is about 3.25 times of the ductile iron base material, and the wear resistance of the cladding layer is about 48.8 times of the ductile iron base material. Compared with the prior art, the invention can greatly improve the surface hardness and wear resistance of the spheroidal graphite cast iron base material under the condition of adopting simpler alloy powder, and has lower cost of repairing or surface modifying the surface defects of the iron castings so as to prolong the service life and widen the application range.
Drawings
FIG. 1 is an optical macroscopic topography of the upper surface of an example fabricated cladding layer;
FIG. 2 is a cross-sectional view of the cladding layer obtained in comparative example 1;
FIG. 3 is a cross-sectional view of the cladding layer obtained in comparative example 2;
FIG. 4 is a cross-sectional profile of a cladding layer made according to an embodiment;
FIG. 5 shows the optical microscopic morphology of the cladding layer obtained in comparative example 1;
FIG. 6 is an optical micro-morphology of the cladding layer produced in the examples;
FIG. 7 is a secondary electron morphology image of a scanning electron microscope of an example cladding layer;
FIG. 8 is a microhardness distribution curve of the cladding layer and the cast iron base material of the ball mill prepared in examples and comparative example 1;
FIG. 9 is a cross-section of an example cladding layer and ball mill cast iron friction wear profile;
FIG. 10 is a wear profile of the cladding layer produced in the examples.
Fig. 11 is a wear profile of spheroidal graphite cast iron.
Detailed Description
The instruments, reagents, materials, etc. used in the examples described below are conventional instruments, reagents, materials, etc. known in the art, and are commercially available. The experimental methods, detection methods, and the like in the examples described below are conventional experimental methods, detection methods, and the like that are known in the prior art unless otherwise specified.
The following examples and comparative examples each use the following steps to prepare a cladding layer:
the method is characterized in that a laser cladding method is adopted to prepare a cladding layer on the surface of a spheroidal graphite cast iron substrate, an existing synchronous powder feeding laser cladding mode is adopted, cladding alloy powder consists of reduced iron powder and ferrovanadium powder with a certain proportion of unequal particle sizes, the laser power is 1000W, the laser pulse frequency is 4500Hz, the duty ratio is 95%, the spot diameter is 2.0mm, the scanning speed is 12mm/s, the lap joint rate is 30%, the powder feeding amount is 6-7 g/min, the powder feeding gas flow is 4.5L/min, and the coaxial shielding gas argon flow is 16L/min. The alloy powder is variable-particle-size alloy powder, the particle size of the reduced iron powder ranges from 100 meshes to 200 meshes, and the particle size of the vanadium iron powder ranges from 400 meshes to 600 meshes. Alloy powders were mixed in a V-blender for 2 hours before laser cladding.
Examples
The alloy powder comprises: 51.5wt.% reduced iron powder, 48.5wt.% vanadic iron powder.
Comparative example 1
The difference from the examples is that the alloy powder comprises: 67.6wt.% reduced iron powder, 32.4wt.% vanadic iron powder.
Comparative example 2
The difference from the examples is that the alloy powder comprises: 66.42wt.% reduced iron powder, 32.4wt.% vanadic iron powder, 1.18wt.% graphite.
Referring to fig. 1, the upper surface of the cladding layer prepared by the embodiment has an optical macroscopic morphology image, and the cladding layer can be seen to have a flat surface and good macroscopic shaping.
Referring to fig. 2, the cross-sectional morphology of the cladding layer obtained in comparative example 1 shows that the cladding layer has significant defects, i.e., larger and more pores are present and associated with crack formation.
Referring to FIG. 3, the cross-sectional morphology of the cladding layer obtained in comparative example 2 shows that the cladding layer has significant defects, i.e., larger and more pores are present with crack formation.
Referring to fig. 4, the cross-sectional morphology of the cladding layer produced in the examples shows that the cladding layer did not find significant cracking and porosity defects.
Referring to fig. 5, the optical microscopic morphology of the cladding layer consisting of a large number of equiaxed crystals and a portion of near equiaxed crystals was produced in the comparative example.
Referring to fig. 6, the optical microscopic morphology of the cladding layer made in the example is composed of a large number of equiaxed crystals and a part of near equiaxed crystals, and a large number of eutectic structures are densely distributed like a skeleton among the crystals of the cladding layer. The average grain diameter of the cladding layer is 1.84 mu m, the larger supercooling degree in the cladding process inhibits the growth of grains, and the cladding layer contains a large amount of in-situ autogenous VC, which can serve as the core of heterogeneous nuclei, and the distribution and grain boundary can prevent the growth of grains.
Referring to fig. 7, the secondary electron morphology image of the scanning electron microscope of the cladding layer prepared in the embodiment successfully obtains a large amount of in-situ autogenous VC by means of graphite reverse transition in the ductile iron substrate despite no graphite added in the cladding powder, and the cladding layer consists of martensite, a large amount of eutectic structures distributed among crystals and in-situ autogenous VC. Because carbon elements in the cladding layer are more consumed, generated cementite participates in eutectic reaction, and a large number of eutectic structures which are uniformly distributed are generated.
Referring to fig. 8, the microhardness distribution curves of the cladding layers prepared in the examples and the comparative examples are 950HV0.2, and the average microhardness of the cladding layers prepared in the examples is greatly improved by about 3.25 times compared with that of the spheroidal graphite cast iron base material.
Referring to fig. 9, the friction wear profile cross section of the example cladding layer and ductile iron substrate. Measuring example cladding layer and ductile ironThe abrasion loss of the base material was 0.126mm 3 And 6.15mm 3 It can be inferred that the wear resistance of the cladding layer of the example was about 48.8 times that of the spheroidal graphite cast iron substrate. The wear-resistant alloy has extremely excellent wear resistance due to the high average hardness, the protection of eutectic structures and the dispersion strengthening effect of in-situ autogenous VC.
Referring to fig. 10 and 11, the wear profiles of the cladding layer and the ball-milled cast iron substrate prepared in the examples are respectively analyzed, and a large number of grooves appear on the wear profile of the surface of the ductile iron substrate, which shows delamination and serious peeling of the substrate, meaning that obvious plastic deformation exists. This is mainly due to the low hardness of the spheroidal graphite cast iron and the presence of graphite particles resulting in an uneven hardness distribution, so that significant flaking and delamination occurs under continuous friction of the grinding ball against the surface of the sample. The wear of the spheroidal graphite cast iron mainly comprises the combined action of adhesive wear, fatigue wear and abrasive particle wear. The abrasion surface of the cladding layer of the embodiment is relatively smooth, and only has a small amount of adhesion marks, and the typical abrasive particle abrasion appearance is shown. The embodiment cladding layer has more excellent hardness, a large number of eutectic structures are densely distributed among crystals, and a large number of in-situ autogenous VC is pinned in the eutectic structures to play a role of a wear-resistant framework to jointly block abrasion.
Although embodiments of the present invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made therein without departing from the spirit and scope of the invention as defined by the appended claims and their equivalents.
Claims (6)
1. A preparation method of a high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of spheroidal graphite cast iron is characterized by comprising the following steps of: and preparing a cladding layer on the surface of the spheroidal graphite cast iron substrate by adopting a laser cladding method, wherein cladding alloy powder consists of reduced iron powder and ferrovanadium powder with a certain proportion of unequal particle sizes.
2. The method for preparing the high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron according to claim 1, which is characterized in that: the alloy powder comprises: 51.5wt.% reduced iron powder, 48.5wt.% vanadic iron powder.
3. The method for preparing the high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron according to claim 2, which is characterized in that: the alloy powder is variable-particle-size alloy powder, the particle size range of the reduced iron powder is 100-200 meshes, and the particle size range of the vanadium iron powder is 400-600 meshes.
4. The method for preparing the high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron according to claim 2, which is characterized in that: the synchronous powder feeding laser cladding mode is adopted, the cladding alloy powder consists of reduced iron powder and ferrovanadium powder with certain proportion and unequal particle sizes, the laser power is 1000W, the pulse frequency is 4500Hz, the duty ratio is 95%, the light spot diameter is 2.0mm, the scanning speed is 12mm/s, the overlap ratio is 30%, the powder feeding amount is 6-7 g/min, the powder feeding gas flow is 4.5L/min, and the coaxial shielding gas argon flow is 16L/min.
5. The method for preparing the high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron according to claim 1, which is characterized in that: and mixing the alloy powder in a V-shaped powder mixer for 1.5-3 hours before laser cladding.
6. A high wear-resisting Fe-based fine-grain laser cladding layer on the surface of spheroidal graphite cast iron is characterized in that: the method for preparing the high-wear-resistance Fe-based fine-grain laser cladding layer on the surface of the spheroidal graphite cast iron according to any one of claims 1 to 5.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202410050719.XA CN117721462A (en) | 2024-01-15 | 2024-01-15 | Fe-based fine-grain laser cladding layer with high wear resistance on surface of spheroidal graphite cast iron and preparation method thereof |
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| Application Number | Priority Date | Filing Date | Title |
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| CN202410050719.XA CN117721462A (en) | 2024-01-15 | 2024-01-15 | Fe-based fine-grain laser cladding layer with high wear resistance on surface of spheroidal graphite cast iron and preparation method thereof |
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| CN117721462A true CN117721462A (en) | 2024-03-19 |
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