CN111607789B - Laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer and preparation method thereof - Google Patents
Laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer and preparation method thereof Download PDFInfo
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- 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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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Abstract
The invention discloses a laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer and a preparation method thereof, wherein the preparation method comprises the following steps: mixing and drying iron-based alloy powder, titanium and vanadium to obtain iron-based composite powder, and laser cladding the obtained iron-based composite powder on the surface of a base material by adopting a laser irradiation in-situ self-generation method, wherein the titanium content is 1-3wt% of the iron-based composite powder, and the vanadium content is 2-5wt% of the iron-based composite powder; the invention also discloses a cladding layer obtained by the method, the method has the advantages of lower cost and capability of obviously improving the surface hardness and the wear resistance of the iron-based alloy, and the obtained cladding layer has the advantages of better surface hardness and wear resistance.
Description
Technical Field
The invention relates to the technical field of laser cladding, in particular to a laser cladding in-situ synthesized carbide particle reinforced iron-based cladding layer and a preparation method thereof.
Background
The laser surface modification is a high and new technology developed in the 70 s of the 20 th century, and the characteristics of high radiation intensity, high directionality and high monochromaticity of the laser are utilized to act on the surface of a component, so that the surface performance of the material is improved. Laser cladding is a kind of laser surface modification, and its principle is that through laser melting of prepared alloy powder, it becomes the main body alloy of cladding layer, and at the same time, high-energy laser beam is used to irradiate metal surface, and a thin layer of base metal is melted, so that the thin layer of metal base surface and cladding alloy are quickly melted, reacted and solidified together to form the cladding layer with special properties, such as high hardness, wear resistance and corrosion resistance. The laser cladding has the characteristics of small thermal deformation of the substrate, metallurgical bonding between the cladding layer and the substrate, easy realization of automatic production and the like, is widely concerned and is applied in various industrial fields.
The iron-based alloy has a series of advantages of low cost, good mechanical property, good machining and welding properties, corrosion resistance and the like, and has wide application. The iron-based alloy is used as a cladding material and has high bonding strength with the surface of a steel material, so that the iron-based alloy is often used in the fields of surface protection and surface repair. But the hardness and wear resistance of the iron-based alloy are to be improved. In order to adapt to the gradual improvement of the social continuous development on the material performance requirement, particularly under the working condition of frictional wear of mechanical equipment, adding hard particles into the iron-based alloy is an important method for improving the hardness and the wear resistance, and ceramic particles are often used as a reinforcing phase of a laser cladding iron-based alloy cladding layer to strengthen the coating performance due to the advantages of high hardness, high melting point, good thermal stability and the like. The addition modes of the reinforcing phase are mainly two, namely an external reinforcing phase method and an in-situ autogenous method.
The manual additional enhancement phase method is simple and convenient, is convenient for regulating and controlling the content of the enhancement phase, but also has the inevitable defects: firstly, the reinforcing phase particles cannot be guaranteed not to be polluted in the processes of preparation, packaging, transportation and addition, impurities are easily introduced into the coating, so that the bonding interface between the reinforcing phase particles and the matrix is not good, even the generation of interface cracks is easily caused, and the expected reinforcing effect cannot be achieved; secondly, it is difficult to control the mixing of the reinforcing phase particles and the coating powder to be uniform and uniform, which is mainly caused by the difference in the particle size and the density of the powder, so that the reinforcing phase particles are not uniformly distributed in the coating, and the reinforcing effect is reduced. The in-situ self-generation method is characterized in that chemical components of the strengthening layer are reasonably configured, and reinforcing phase particles which are not originally present in the strengthening layer are self-generated in situ through chemical reaction in the preparation and formation process of the strengthening layer, compared with an external reinforcing phase method, the reinforcing phase of the in-situ self-generation method is a thermodynamically stable phase which is nucleated and grows in situ from an alloy melt, so that the surface of the reinforcing phase is free of pollution, the problem of poor compatibility with a base body is solved, the interface bonding strength is high, and the types, sizes, quantities and even distribution conditions of the reinforcing phase can be regulated and controlled by selecting proper components and processes; the method has the advantages of simple process, low cost, easy popularization and application and the like, and has wide application space.
If the Chinese patent with the granted publication number of CN108339976B discloses powder for laser cladding in-situ synthesized vanadium carbide reinforced iron-based alloy and a preparation method thereof, the mass percentages of the elements of the alloy powder prepared by a vacuum atomization method are C4.00-4.40%, V16.00-18.00%, Cr 8.00-10.00%, Si 0.90-1.30%, Mo 1.00-2.00%, Mn 0.90-1.20%, Ni 0.40-0.70%, Al 0.30-0.50%, the total mass fraction of P and S is less than or equal to 0.03%, O is less than or equal to 300ppm, and the balance is Fe. By using CO2The alloy powder is laser-cladded on the surface of a low-carbon alloy steel base material in a synchronous powder feeding mode of a laser processing system, the powder of a cladding layer absorbs laser energy to form a molten pool on the surface of the base material, and C element and V element in the molten pool react to generate in-situ self-generated V8C7The ceramic reinforcing phase, and meanwhile, the cladding layer and the base material form good metallurgical bonding. Preparation of in situ authigenic V8C7The particle reinforced iron-based alloy laser cladding layer can obviously improve the hardness and the wear resistance of the surface of a low-alloy steel member, but the ceramic particle hard phase of the method is VC, the cost of vanadium is higher, and a finished product needs to be providedThe method is lower in cost and can improve the surface hardness and the wear resistance of the iron-based alloy.
Disclosure of Invention
Aiming at the defects in the prior art, the first purpose of the invention is to provide a preparation method of an iron-based cladding layer reinforced by laser cladding in-situ authigenic carbide particles, which has the advantages of lower cost and capability of obviously improving the surface hardness and the wear resistance of an iron-based alloy.
The second purpose of the invention is to provide a laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer which has the advantages of better surface hardness and wear resistance.
In order to achieve the first object, the invention provides the following technical scheme: a preparation method of a laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer comprises the following steps:
mixing and drying iron-based alloy powder, a titanium additive and a vanadium additive to obtain iron-based composite powder, and carrying out laser cladding on the iron-based composite powder on the surface of a substrate by adopting a laser irradiation in-situ autogenous method, wherein the titanium content is 1-3wt% of the iron-based composite powder, the vanadium content is 2-5wt% of the iron-based composite powder, and the iron-based alloy powder comprises the following elements in percentage by mass: 0.7-1%, Cr: 17-20%, Ni: 4-5%, Mn: less than or equal to 1 percent, Mo: 1-2%, B: 1-2%, Si: less than or equal to 1 percent, Nb: 2-3% of Fe and the balance of Fe.
By adopting the technical scheme, the invention adopts a laser irradiation in-situ self-generation method, iron-based composite powder absorbs laser beam irradiation energy on the surface of a base material to form a molten pool, Ti, V elements and C in the molten pool react to generate a large amount of fine and dispersed TiC and VC particles in situ, meanwhile, a cladding layer and the base material form good metallurgical bonding, the microhardness value of the cladding layer reaches over 800Hv and has good wear resistance, and the addition of titanium enables the hard phase of ceramic particles to be TiC and VC, thereby further enhancing the hardness and wear resistance of the cladding layer, simultaneously reducing the consumption of vanadium and lowering the cost.
The invention adds vanadium and titanium, TiC granule has high hardness, high elastic modulus, the thermodynamic property is stable, it is an ideal ceramic reinforcement phase, V is the forming element of strong carbide, reaction product VC with carbon has similar property with TiC, and it has better wettability to the steel substrate, and TiC and VC and iron-based alloy wettability are better, the interface bonding strength is high, adopt the laser cladding home position autogenous method to form ceramic granule hard phase TiC and VC, TiC and VC granule of home position autogenous are from the direct nucleation of the metal melt, grow up, the thermodynamic property is stable, the interface bonding strength with substrate is higher, difficult to produce the crackle, and the surface of reinforcement phase is pollution-free, the purity is higher, and the reinforcement phase is difficult to appear and agglomerate or segregate, the granule size produced by the reaction is fine and relatively dispersed. In addition, the TiC and the VC are in face-centered cubic structures, the lattice constants of the TiC and the VC are close, the compatibility is good, fine TiC and VC particles are easy to mutually combine and adhere to each other in the solidification process of a molten pool to grow into a composite carbide reinforcement, the formation of a reinforced phase is facilitated, and therefore the surface hardness and the wear resistance of the iron-based alloy are remarkably improved.
In addition, the iron-based alloy powder provided by the invention has good corrosion resistance, and has good wear resistance after being reinforced by adding titanium and vanadium in-situ authigenic particles, and when vanadium and titanium are compositely added in the invention, titanium can promote other carbide stabilizing elements to react with carbon to be separated out in the form of carbide, so that the carbide number in a final cladding layer is large, and simultaneously, the addition of vanadium can play a role in refining grains, so that the carbide number in the final cladding layer is large, and the grains are fine, more importantly, when titanium and vanadium are compositely added, two carbides can play a role in mutually inhibiting growth to a certain extent, and the migration of grain boundaries is hindered, so that the generated carbide is finer, the grains of the final cladding layer are fine, the carbide is finer, and the hardness and the wear resistance are improved. Finally, the iron-based composite powder obtained by combining the iron-based alloy powder of the system with vanadium and titanium in a specific ratio is used for in-situ self-generation TiC and VC in the laser cladding process provided by the invention, the obtained carbide of the cladding layer has optimal form, distribution and quantity, the hardness and the wear resistance of the cladding layer are obviously improved, the cladding layer has no pore cracks, and the cladding performance is good.
On the basis of forming TiC and VC reinforced phases by in-situ self-generation of vanadium and titanium raw materials, the proportion of iron-based alloy powder, titanium and vanadium is controlled, the finally obtained cladding layer has compact tissue, no defects such as air holes and cracks, and the like, and is well metallurgically bonded with a base material, and the in-situ self-generated TiC and VC particles are fine and dispersed. The preparation process of the laser cladding in-situ autocarbide particle reinforced iron-based cladding layer has the advantages of simplicity, convenience in operation, easiness in automation realization, no pollution and the like, cladding is not required to be carried out under a vacuum condition, and the size of a workpiece is not limited, so that the laser cladding in-situ autocarbide particle reinforced iron-based cladding layer can be used for repairing a complex surface, and has remarkable economic and social benefits in material surface modification.
The invention is further configured to: the iron-based alloy powder comprises the following elements in percentage by mass: 0.7-1%, Cr: 17-20%, Ni: 4-5%, Mn: 0.5-1%, Mo: 1-2%, B: 1-2%, Si: 0.5-1%, Nb: 2-3% of Fe and the balance of Fe.
The invention is further configured to: the particle size range of the iron-based composite powder is 40-100 mu m, the average particle size D50 is 50-70 mu m, the fluidity is 30-40s/100g, and the oxygen content is less than or equal to 300 ppm.
By adopting the technical scheme, the success rate of the cladding process is improved by controlling the granularity and the flowability of the iron-based composite powder, the performance of the cladding layer is optimal, the hardness and the wear resistance are improved by controlling the oxygen content, the cladding layer does not generate cracks and pores, and the structure of the cladding layer is uniform.
The invention is further configured to: the iron-based composite powder is obtained by: uniformly mixing the iron-based alloy powder, titanium and vanadium, heating for 1.5-2.5h at 70-100 ℃, and drying to obtain the titanium-based alloy.
The invention is further configured to: the vanadium additive is vanadium powder or ferrovanadium powder, preferably ferrovanadium powder with the vanadium content of 40%.
The invention is further configured to: the titanium additive is selected from titanium powder or ferrotitanium powder, preferably ferrotitanium powder with 30% of titanium content.
By adopting the technical scheme, vanadium and titanium with specific proportions can be provided, the hardness and the wear resistance of the cladding layer are improved, and in addition, pure titanium powder or pure vanadium powder is compared with ferrovanadium powder and ferrotitanium powder, although the finally added vanadium content and titanium content are the same, the prices of the ferrovanadium powder and the ferrotitanium powder are far lower than those of the pure titanium powder or the pure vanadium powder.
The invention is further configured to: carrying out laser cladding after the base material is pretreated, wherein the base material pretreatment operation comprises the following steps: the substrate surface was polished with an angle grinder and cleaned with acetone.
The invention is further configured to: the laser cladding process parameters are as follows: the laser power is 1600-3000W, the scanning speed is 6-10mm/s, the spot diameter is 2.5-5mm, and the powder feeding rate is 15-25 g/min.
The invention is further configured to: the lapping rate in the laser cladding process is 30-70%, argon is used as protective gas, and the flow of the argon is 2-10L/min.
By adopting the technical scheme, the cladding layer with the macroscopic morphology, the microstructure and the mechanical property meeting the requirements is finally obtained by controlling the process parameters in the laser cladding process, particularly controlling the laser power, the scanning speed, the powder feeding rate and the spot diameter.
In order to achieve the second object, the invention provides the following technical scheme: a laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer is prepared by the method.
By adopting the technical scheme, the metal iron resource is rich, the price is low, the application is wide, the iron-based alloy is used as the basic phase of the cladding layer, the titanium carbide and the vanadium carbide are used as the reinforcing phase, the cladding layer obtained by the method provided by the invention has compact structure, no defects of pores, cracks and the like, is in good metallurgical bonding with the base material, and has very obvious effect on the improvement of the surface hardness and the wear resistance of the iron-based alloy.
In conclusion, the invention has the following beneficial effects:
1. according to the invention, a laser irradiation in-situ self-generation method is adopted, the iron-based composite powder absorbs laser beam irradiation energy on the surface of a base material to form a molten pool, Ti, V elements and C in the molten pool react to generate a large amount of fine and dispersed TiC and VC particles in situ, meanwhile, a cladding layer and the base material form good metallurgical bonding, the microhardness value of the cladding layer reaches more than 800Hv, and simultaneously, the cladding layer has good wear resistance, and the addition of titanium enables the hard phase of ceramic particles to be TiC and VC, so that the hardness and wear resistance of the cladding layer are further enhanced, the amount of vanadium is reduced, and the cost is reduced;
2. the invention combines the iron-based alloy powder of a specific proportion system with the vanadium and the titanium of a specific proportion to obtain the iron-based composite powder, the iron-based composite powder is used for in-situ self-generation TiC and VC in the laser cladding process provided by the invention, the obtained carbide of the cladding layer has optimal shape, distribution and quantity, the in-situ self-generation TiC and VC particles are fine and dispersed, the hardness and the wear resistance of the obtained cladding layer are obviously improved, and the cladding layer has compact structure, no pore crack and good cladding performance;
3. the preparation process of the laser cladding in-situ autocarbide particle reinforced iron-based cladding layer has the advantages of simplicity, convenience in operation, easiness in automation realization, no pollution and the like, cladding is not required to be carried out under a vacuum condition, and the size of a workpiece is not limited, so that the laser cladding in-situ autocarbide particle reinforced iron-based cladding layer can be used for repairing a complex surface, and has remarkable economic and social benefits in material surface modification.
Drawings
FIG. 1 is a schematic diagram of a frictional wear test in the present invention.
Detailed Description
The present invention will be described in further detail with reference to examples.
Aiming at the problems that the existing laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer takes iron-based alloy as a basic phase and TiC and VC as reinforcing phases, if the TiC and VC particles are directly added, the defects of air holes, cracks and the like are easy to appear during laser cladding, or the reinforcing phases and the cladding layer have poor wettability, the reinforcing phases are agglomerated and the like, so that the cladding layer is easy to peel off, the mechanical property is deteriorated, and the use of the cladding layer is influenced, therefore, the TiC and VC reinforcing phases are obtained by adopting an in-situ authigenic method, and the following technical scheme is obtained through a large number of tests:
a method for laser cladding in-situ autocarbide particle reinforced iron-based cladding layer comprises the following steps:
pretreatment of a base material: polishing the surface of a substrate by using an angle grinder and cleaning the surface of the substrate by using acetone, wherein the substrate can be a low-carbon steel substrate, a medium-carbon steel substrate or a high-carbon steel substrate, and the following example takes a 45# steel substrate as an example for illustration;
preparation of iron-based composite powder: mixing iron-based alloy powder, a vanadium additive and a titanium additive which are prepared by vacuum gas atomization in a mixer for 90-150min, heating at 70-100 ℃ for 1.5-2.5h after uniform mixing, and drying to obtain iron-based composite powder, wherein the particle size range of the iron-based composite powder is 40-100 mu m, the average particle size D50 is 50-70 mu m, the fluidity is 30-40s/100g, and the oxygen content is less than or equal to 300 ppm;
the vanadium content is 1-3wt% of the iron-based composite powder, the titanium content is 2-5wt% of the iron-based composite powder, the vanadium additive can be vanadium powder or ferrovanadium powder, the ferrovanadium powder can be ferrovanadium powder with the vanadium content of 40% or ferrovanadium powder with other vanadium contents, and only the vanadium content in the iron-based composite powder needs to be controlled to be 1-3wt%, the ferrovanadium powder or ferrovanadium powder with the particle size of 40-100 mu m is preferred, and the ferrovanadium powder with the particle size of 40-100 mu m and the vanadium content of 40% is more preferred; similarly, the titanium additive can be titanium powder or ferrotitanium powder, preferably titanium powder or ferrotitanium powder with the particle size of 40-100 μm, the ferrotitanium powder can be ferrotitanium powder with the vanadium content of 30%, and can also be ferrotitanium powder with other titanium contents, only the titanium content in the iron-based composite powder needs to be controlled to be 2-5wt%, more preferably ferrotitanium powder with the particle size of 40-100 μm and the titanium content of 30%, and if 100g of iron-based composite powder with the vanadium content of 1 wt% of the iron-based composite powder needs to be prepared, 1g of vanadium powder or 2.5g of ferrovanadium powder with the vanadium content of 40% can be added;
the iron-based alloy powder is prepared by vacuum gas atomization, the iron-based alloy powder is prepared and then subjected to particle size screening, the iron-based alloy powder with the particle size range of 40-100 mu m is mixed with vanadium additives and titanium additives with the particle size of 40-100 mu m, and the iron-based alloy powder comprises the following elements in percentage by mass: 0.7-1%, Cr: 17-20%, Ni: 4-5%, Mn: less than or equal to 1 percent, Mo: 1-2%, B: 1-2%, Si: less than or equal to 1 percent, Nb: 2-3%, the balance being Fe, more preferably C: 0.7-1%, Cr: 17-20%, Ni: 4-5%, Mn: 0.5-1%, Mo: 1-2%, B: 1-2%, Si: 0.5-1%, Nb: 2-3% of Fe, and the balance of Fe;
laser cladding: feeding the iron-based composite powder into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, wherein CO is used for laser cladding2A laser processing system. The laser cladding process parameters can affect the macroscopic morphology, the microstructure and the mechanical property of a cladding layer, and the main parameters affecting the cladding layer quality comprise laser power, buckling and drawing speed, powder feeding rate, spot diameter and the like. The laser power is increased and the scanning speed is reduced, so that more powder is melted, the bonding strength is improved, and the cracking tendency is reduced. The powder feeding rate is increased, the thickness of the cladding layer is increased, the dilution rate is reduced, but the crack sensitivity is increased.
Through a large number of experiments, the following laser cladding process parameters are obtained to prepare the cladding layer meeting the requirements, and the adopted laser cladding parameters are as follows: argon is used as protective gas, the laser power is 1600-3000W, the scanning speed is 6-10mm/s, the spot diameter is 2.5-5mm, the lap joint rate is 30-70%, the powder feeding rate is 15-25g/min, and the argon flow is 2-10L/min.
The preparation of the iron-based alloy powder is that metal raw materials are mixed according to iron-based alloy components and then melted in a vacuum state to obtain liquid metal, the liquid metal is atomized to obtain the iron-based alloy powder, the principle of vacuum atomization is the process of crushing liquid metal flow into small liquid drops by high-speed airflow and solidifying the small liquid drops into powder, the iron-based alloy powder is the prior art, and the preparation of the iron-based alloy powder is the prior art and is not detailed in the invention.
Example 1
A method for laser cladding in-situ autocarbide particle reinforced iron-based cladding layer comprises the following steps:
machine material pretreatment: polishing the surface of a 45# steel substrate by using an angle grinder and cleaning the surface by using acetone to obtain a flat and clean surface;
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum gas atomization and is subjected to particle size screening, the particle size range of the obtained iron-based alloy powder is 40-100 mu m, the average particle size D50 is 65.8 mu m, the flowability is 35.5s/100g, the oxygen content is 285ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.8%, Cr: 17.82%, Ni: 4.32%, Mn: 0.54%, Mo: 1.33%, B: 1.74%, Si: 0.77%, Nb: 2.51 percent, and the balance being Fe;
then mechanically mixing iron-based alloy powder, ferrotitanium powder with the particle size of 40-100 microns and ferrovanadium powder with the particle size of 40-100 microns in a mixer for 2 hours, heating at 80 ℃ for 2 hours after uniformly mixing, and drying to obtain iron-based composite powder, wherein the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%, the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%, the addition amount of the ferrotitanium powder is 10% of the mass of the iron-based composite powder, and the addition amount of the ferrovanadium powder is 4.3% of the mass of the iron-based composite powder;
laser cladding: feeding the iron-based composite powder for cladding into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, wherein CO is used for laser cladding2The laser processing system adopts the following laser cladding parameters: argon is used as a protective gas, the laser power is 2400W, the scanning speed is 8mm/s, the spot diameter is 3.18mm, the lap joint rate is 50%, the powder feeding rate is 20g/min, and the argon flow is 3L/min.
Example 2
A method for laser cladding of an in-situ autocarbide particle reinforced iron-based cladding layer is carried out according to the method in the embodiment 1, and the difference is that:
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum atomization and is subjected to particle size screening, the particle size range of the iron-based alloy powder obtained by screening is 40-100 mu m, the average particle size D50 is 68.9 mu m, the fluidity is 32.3s/100g, the oxygen content is 293ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.82%, Cr: 17.25%, Ni: 4.89%, Mn: 0.66%, Mo: 1.61%, B: 1.59%, Si: 0.72%, Nb: 2.12 percent, and the balance being Fe;
then mechanically mixing iron-based alloy powder, ferrotitanium powder with the particle size of 40-100 microns and ferrovanadium powder in a mixer for 2 hours, heating at 80 ℃ for 2 hours after uniformly mixing, and drying to obtain iron-based composite powder, wherein the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%, the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%, the addition amount of the ferrotitanium powder is 12% of the mass of the iron-based composite powder, and the addition amount of the ferrovanadium powder is 2.5% of the mass of the iron-based composite powder;
laser cladding: feeding the iron-based composite powder for cladding into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, wherein CO is used for laser cladding2The laser processing system adopts the following laser cladding parameters: argon is used as a protective gas, the laser power is 2400W, the scanning speed is 8mm/s, the spot diameter is 3.18mm, the lap joint rate is 50%, the powder feeding rate is 20g/min, and the argon flow is 3L/min.
Example 3
A method for strengthening an iron-based cladding layer by laser cladding in-situ autocarbide particles is carried out according to the method in the embodiment 1, except that,
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum atomization and is subjected to particle size screening, the particle size range of the screened iron-based alloy powder is 40-100 mu m, the average particle size D50 is 58.4 mu m, the fluidity is 36.1s/100g, the oxygen content is 279ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.73%, Cr: 17.55%, Ni: 4.13%, Mn: 0.72%, Mo: 1.31%, B: 1.67%, Si: 0.81%, Nb: 2.24%, the balance being Fe;
then mechanically mixing iron-based alloy powder, ferrotitanium powder with the particle size of 40-100 microns and ferrovanadium powder in a mixer for 2 hours, heating at 80 ℃ for 2 hours after uniformly mixing, and drying to obtain iron-based composite powder, wherein the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%, the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%, the addition amount of the ferrotitanium powder is 6.7% of the mass of the iron-based composite powder, and the addition amount of the ferrovanadium powder is 6.3% of the mass of the iron-based composite powder;
laser cladding: feeding the iron-based composite powder for cladding into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, wherein CO is used for laser cladding2The laser processing system adopts the following laser cladding parameters: argon is used as a protective gas, the laser power is 2400W, the scanning speed is 8mm/s, the spot diameter is 3.18mm, the lap joint rate is 50%, the powder feeding rate is 20g/min, and the argon flow is 3L/min.
Example 4
A method for laser cladding in-situ autocarbide particle reinforced iron-based cladding layer comprises the following steps:
machine material pretreatment: polishing the surface of a 45# steel substrate by using an angle grinder and cleaning the surface by using acetone to obtain a flat and clean surface;
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum gas atomization and is subjected to particle size screening, the particle size range of the iron-based alloy powder obtained by screening is 40-100 mu m, the average particle size D50 is 63.1 mu m, the flowability is 34.6s/100g, the oxygen content is 285ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.78%, Cr: 17.62%, Ni: 4.56%, Mn: 0.78%, Mo: 1.55%, B: 1.48%, Si: 0.79%, Nb: 2.36 percent, and the balance being Fe;
mechanically mixing iron-based alloy powder, ferrotitanium powder with the particle size of 40-100 microns and ferrovanadium powder in a mixer for 90min, heating at 70 ℃ for 2.5h after uniform mixing, and drying to obtain iron-based composite powder, wherein the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%, the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%, the addition amount of the ferrotitanium powder is 6.7% of the mass of the iron-based composite powder, and the addition amount of the ferrovanadium powder is 2.5% of the mass of the iron-based composite powder;
laser cladding: feeding the iron-based composite powder for cladding into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, and carrying out laser cladding to ensure that the cladding layer is formedWith CO2The laser processing system adopts the following laser cladding parameters: argon is used as a protective gas, the laser power is 1600W, the scanning speed is 6mm/s, the spot diameter is 2.5mm, the lap joint rate is 30%, the powder feeding rate is 15g/min, and the argon flow is 2L/min.
Example 5
A method for laser cladding in-situ autocarbide particle reinforced iron-based cladding layer comprises the following steps:
machine material pretreatment: polishing the surface of a 45# steel substrate by using an angle grinder and cleaning the surface by using acetone to obtain a flat and clean surface;
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum atomization and is subjected to particle size screening, the particle size range of the iron-based alloy powder obtained by screening is 40-100 mu m, the average particle size D50 is 67.2 mu m, the fluidity is 37.8s/100g, the oxygen content is 300ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.82%, Cr: 17.69%, Ni: 4.71%, Mn: 0.83%, Mo: 1.62%, B: 1.72%, Si: 0.83%, Nb: 2.61%, the balance being Fe;
then mechanically mixing iron-based alloy powder, ferrotitanium powder with the particle size of 40-100 microns and ferrovanadium powder in a mixer for 150min, heating at 100 ℃ for 1.5h after uniformly mixing, and drying to obtain iron-based composite powder, wherein the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%, the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%, the addition amount of the ferrotitanium powder is 17% of the mass of the iron-based composite powder, and the addition amount of the ferrovanadium powder is 7.5% of the mass of the iron-based composite powder;
laser cladding: feeding the iron-based composite powder for cladding into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, wherein CO is used for laser cladding2The laser processing system adopts the following laser cladding parameters: argon is used as a protective gas, the laser power is 3000W, the scanning speed is 10mm/s, the spot diameter is 5mm, the lap joint rate is 70%, the powder feeding rate is 25g/min, and the argon flow is 10L/min.
Example 6
A method for laser cladding of an in-situ autocarbide particle reinforced iron-based cladding layer is carried out according to the method in the embodiment 1, and the difference is that:
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum atomization and is subjected to particle size screening, the particle size range of the iron-based alloy powder obtained by screening is 40-100 mu m, the average particle size D50 is 64.3 mu m, the fluidity is 37.3s/100g, the oxygen content is 300ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.7%, Cr: 17%, Ni: 4%, Mn: 0.5%, Mo: 1%, B: 1%, Si: 0.5%, Nb: 2 percent and the balance of Fe.
Example 7
A method for laser cladding of an in-situ autocarbide particle reinforced iron-based cladding layer is carried out according to the method in the embodiment 1, and the difference is that:
preparation of iron-based composite powder: the iron-based alloy powder is prepared by vacuum atomization and is subjected to particle size screening, the particle size range of the iron-based alloy powder obtained by screening is 40-100 mu m, the average particle size D50 is 68.8 mu m, the flowability is 34.1s/100g, the oxygen content is 300ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 1%, Cr: 20%, Ni: 5%, Mn: 1%, Mo: 2%, B: 2%, Si: 1%, Nb: 3 percent and the balance of Fe.
Example 8
A method for laser cladding of an in-situ autocarbide particle reinforced iron-based cladding layer is carried out according to the method in the embodiment 1, and the difference is that: in the preparation of the iron-based composite powder, iron-based alloy powder, titanium powder with the particle size of 40-100 mu m and vanadium powder are mechanically mixed in a mixer, wherein the addition amount of the titanium powder is 5% of the mass of the iron-based composite powder, and the addition amount of the vanadium powder is 3% of the mass of the iron-based composite powder.
Comparative example
Comparative example 1
A method for laser cladding in-situ autocarbide particle reinforced iron-based cladding layer comprises the following steps:
the iron-based alloy powder is prepared by vacuum atomization, the particle size range of the iron-based alloy powder is 40-100 mu m, the average particle size D50 is 67.7 mu m, the fluidity is 37.1s/100g, the oxygen content is 300ppm, and the iron-based alloy powder comprises the following components in percentage by mass: c: 0.8%, Cr: 17.82%, Ni: 4.32%, Mn: 0.54%, Mo: 1.33%, B: 1.74%, Si: 0.77%, Nb: 2.51 percent and the balance of Fe.
Laser cladding: feeding the iron-based alloy powder for cladding into a coaxial powder feeder by adopting a laser irradiation in-situ synthesis method, adjusting laser cladding process parameters under the protection of argon, preparing a cladding layer on the surface of a substrate by adopting a coaxial powder feeding laser cladding mode, wherein CO is used for laser cladding2The laser processing system adopts the following laser cladding parameters: argon is used as a protective gas, the laser power is 3000W, the scanning speed is 10mm/s, the spot diameter is 5mm, the lap joint rate is 70%, the powder feeding rate is 25g/min, and the argon flow is 10L/min.
Comparative example 2
A method for strengthening an iron-based cladding layer by laser cladding in-situ autocarbide particles is carried out according to the method in the embodiment 1, except that,
preparation of iron-based composite powder: mechanically mixing iron-based alloy powder and ferrotitanium powder with the particle size of 40-100 mu m in a mixer for 2 hours, heating at 80 ℃ for 2 hours after uniform mixing, and drying to obtain iron-based composite powder, wherein the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%, and the addition amount of the ferrotitanium powder is 10% of the mass of the iron-based composite powder.
Comparative example 3
A method for strengthening an iron-based cladding layer by laser cladding in-situ autocarbide particles is carried out according to the method in the embodiment 1, except that,
preparation of iron-based composite powder: mechanically mixing iron-based alloy powder and ferrovanadium powder with the particle size of 40-100 mu m in a mixer for 2 hours, heating at 80 ℃ for 2 hours after uniformly mixing, and drying to obtain the iron-based composite powder, wherein the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%, and the addition amount of the ferrovanadium powder is 4.3% of the mass of the iron-based composite powder.
Comparative example 4
A method for strengthening an iron-based cladding layer by laser cladding in-situ autocarbide particles is carried out according to the method in the embodiment 1, except that,
when the iron-based composite powder is prepared, the addition amount of the ferrotitanium powder is 20% of the mass of the iron-based composite powder, and the ferrotitanium powder is ferrotitanium powder with the titanium content of 30%.
Comparative example 5
A method for strengthening an iron-based cladding layer by laser cladding in-situ autocarbide particles is carried out according to the method in the embodiment 1, except that,
when the iron-based composite powder is prepared, the addition amount of the ferrotitanium powder is 3.4 percent of the mass of the iron-based composite powder, and the ferrotitanium powder is ferrotitanium powder with the titanium content of 30 percent.
Comparative example 6
A method for reinforcing an iron-based cladding layer by laser cladding in-situ autocarbide particles is carried out according to the method in the embodiment 1, and is characterized in that the addition amount of ferrovanadium powder is 1% of the mass of iron-based composite powder, and the ferrovanadium powder is ferrovanadium powder with the vanadium content of 40%.
Performance detection
The laser cladding layers obtained in examples 1 to 8 and comparative examples 1 to 6 were examined for hardness values and wear resistance properties.
The hardness value detection method comprises the following steps: the micro-hardness distribution of the alloy is tested by using an HVS-1000 type Vickers hardness tester, the normal load is 300g, and the loading time is 15 s. In order to ensure the accuracy of data, 3 points are measured at the same depth, the average value of the 3 points is taken as the microhardness value of the cladding layer at the depth, and the measured Vickers hardness is shown in the following table 1.
TABLE 1 micro-hardness table
As can be seen from tables 1 and 2 above, the cladding layers obtained by the method of the present invention are excellent in hardness and wear resistance.
The wear resistance detection method comprises the following steps: adopting an MRH-3W type high-speed ring block friction wear testing machine to test a ring and a test block according to GB/T12444-2006 Metal Material wear test methodSliding wear test the wear resistance of the cladding layer is tested, the schematic diagram of the ring block friction wear test is shown in figure 1, the test parameters are that the applied load is 150N, the abrasion time is 60min, and the rotating speed is 200 r/min. The test specimen size was 19X 12mm3And selecting GCr15 steel with the Rockwell hardness of 62.5HRC as a grinding pair, and machining the surface of the sample before testing to ensure the similar surface smoothness. The samples were cleaned and dried before and after the test, and then weighed by an analytical balance and the loss on abrasion (loss on abrasion: weight before abrasion-weight after abrasion) was calculated with an analytical balance precision of 0.0001g, and the measurement results are shown in table 2 below.
TABLE 2 abrasion resistance test
As can be seen from table 1 and table 2 above, the hardness and wear resistance of the cladding layer obtained by the method provided by the present invention are excellent, the iron-based alloy powder is mixed with the iron-titanium powder and the ferrovanadium powder in example 1 and then used for laser cladding to obtain the cladding layer, while the iron-based alloy powder is directly used for laser cladding in comparative example 1 to obtain the cladding layer, referring to the detection results in comparative example 1 and example 1, it can be seen that the hardness of the cladding layer in comparative example 1 is much lower than that of the cladding layer obtained in example 1, while the wear loss in comparative example 1 is much higher than that of the cladding layer in example 1, and it can be seen that the hardness and wear resistance of the cladding layer obtained without adding titanium and vanadium in comparative example 1 are much lower than those of the cladding layer obtained after adding titanium and vanadium in example 1; referring to the detection data in example 1, comparative example 2 and comparative example 3, it can be seen that the hardness and wear resistance of the cladding layer obtained by cladding after mixing the iron-based alloy powder with only ferrotitanium powder or only ferrovanadium powder are lower than those of the cladding layer obtained by cladding after mixing the iron-based alloy powder with ferrotitanium powder and ferrovanadium powder; referring to comparative example 4 again, it can be seen that when the addition amount of the ferrotitanium powder is too much, that is, the content of titanium in the iron-based composite powder is too high, although the hardness after laser cladding is obviously improved, on one hand, the wear resistance of the cladding layer is deteriorated due to coarse and uneven distribution of carbides, and on the other hand, when the content of titanium is too much, the carbide form is large, and the obtained cladding layer is also easy to crack; referring to the comparative example 5 again, when the addition amount of the ferrotitanium powder is too small, namely the content of titanium in the iron-based composite powder is too small, the hardness and the wear resistance of the cladding layer are far lower than the mechanical properties of the cladding layer in the example; referring to the arrangement in the comparative example 6, it can be seen that when the addition amount of the ferrovanadium powder is too low, that is, the content of vanadium in the iron-based composite powder is too low, the mechanical property of the cladding layer is lower than that of the cladding layer in the example, and the functions of grain refinement and particle reinforcement cannot be achieved obviously.
And finally, mixing iron-based alloy powder, vanadium and titanium to obtain the iron-based composite powder, wherein when the content of the titanium is 1-3wt% of the iron-based composite powder and the content of the vanadium is 2-5wt% of the iron-based composite powder, the structure, the mechanical property and the cladding property of the obtained cladding layer, namely the cladding success rate, are optimal.
Referring to the detection data in examples 1 and 8, when the iron-based composite powder is prepared, vanadium powder, ferrovanadium powder and titanium powder and ferrotitanium powder are selected as the addition forms of vanadium and titanium, the hardness and the wear resistance of the finally obtained cladding layer are similar, from the raw material cost, the price of vanadium powder in the current market is more than ten times of the price of ferrovanadium powder, the titanium powder is similar to the ferrotitanium powder, and the vanadium powder and the ferrovanadium powder are added, so that the cost of the vanadium powder is much higher than that of the ferrovanadium powder even if the vanadium content of the iron-based composite powder is the same, and the addition forms of vanadium and titanium in the application document are preferably ferrotitanium powder and ferrovanadium powder, so that the cost can be further reduced.
The present embodiment is only for explaining the present invention, and it is not limited to the present invention, and those skilled in the art can make modifications of the present embodiment without inventive contribution as needed after reading the present specification, but all of them are protected by patent law within the scope of the claims of the present invention.
Claims (10)
1. A preparation method of a laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer is characterized by comprising the following steps:
mixing and drying iron-based alloy powder, a titanium additive and a vanadium additive to obtain iron-based composite powder, and carrying out laser cladding on the iron-based composite powder on the surface of a substrate by adopting a laser irradiation in-situ self-generation method;
wherein, the vanadium content is 1-3wt% of the iron-based composite powder, the titanium content is 2-5wt% of the iron-based composite powder, and the mass percentages of the elements of the iron-based alloy powder are C: 0.7-1%, Cr: 17-20%, Ni: 4-5%, Mn: less than or equal to 1 percent, Mo: 1-2%, B: 1-2%, Si: less than or equal to 1 percent, Nb: 2-3% of Fe and the balance of Fe.
2. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer of claim 1, wherein the iron-based alloy powder comprises the following elements in percentage by mass: 0.7-1%, Cr: 17-20%, Ni: 4-5%, Mn: 0.5-1%, Mo: 1-2%, B: 1-2%, Si: 0.5-1%, Nb: 2-3% of Fe and the balance of Fe.
3. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer as claimed in claim 1, wherein the particle size range of the iron-based alloy powder is 40-100 μm, the average particle size D50 is 50-70 μm, the flowability is 30-40s/100g, and the oxygen content is less than or equal to 300 ppm.
4. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer as claimed in claim 1, wherein the iron-based composite powder is obtained by: uniformly mixing the iron-based alloy powder, titanium and vanadium, heating for 1.5-2.5h at 70-100 ℃, and drying to obtain the titanium-based alloy.
5. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer as claimed in claim 1, wherein the vanadium additive is vanadium powder or ferrovanadium powder with vanadium content of 40 wt%.
6. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer as claimed in claim 1, wherein the titanium additive is selected from titanium powder or ferrotitanium powder with 30wt% of titanium.
7. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer as claimed in claim 1, wherein the laser cladding is performed after the base material is pretreated, and the base material pretreatment operation comprises: the substrate surface was polished with an angle grinder and cleaned with acetone.
8. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer according to claim 1, wherein the laser cladding process parameters are as follows: the laser power is 1600-3000W, the scanning speed is 6-10mm/s, the spot diameter is 2.5-5mm, and the powder feeding rate is 15-25 g/min.
9. The method for preparing the laser cladding in-situ authigenic carbide particle reinforced iron-based cladding layer as claimed in claim 1, wherein the overlap ratio is 30% -70% in the laser cladding process, argon is used as shielding gas, and the flow of the argon is 2-10L/min.
10. A laser cladding in-situ autocarbide particle reinforced iron-based cladding layer, characterized by being obtained by the preparation method of any one of claims 1-9.
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