CN112404672B - Composite powder particles of titanium carbide phase reinforced iron-based surfacing alloy and application method thereof - Google Patents
Composite powder particles of titanium carbide phase reinforced iron-based surfacing alloy and application method thereof Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/32—Selection of soldering or welding materials proper with the principal constituent melting at more than 1550 degrees C
- B23K35/325—Ti as the principal constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/40—Making wire or rods for soldering or welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/18—Submerged-arc welding
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/18—Submerged-arc welding
- B23K9/186—Submerged-arc welding making use of a consumable electrodes
Abstract
A composite powder particle of titanium carbide phase reinforced iron-based surfacing alloy and an application method thereof are adopted, the composite powder particle with the particle size of 10-15 meshes and an H08A solid welding wire serving as an electric arc carrier are prepared by the steps of sieving and weighing powder components, dry mixing the powder components, adding water glass to the mixed powder for wet mixing, rotationally bonding and granulating the wet powder, sintering the powder particles at low temperature, sieving the powder particles and the like, the composite powder particle is optimally configured, the surfacing current value is controlled to be 440-460A, the welding speed is regulated and controlled in a layered mode, and submerged arc surfacing is carried out to enable a composite powder particle melt and a solid welding wire melt drop to be completely fused into an integrated surfacing molten pool, so that the iron-based surfacing alloy with the titanium carbide phase as a main wear-resistant phase is obtained. The composite powder particles can be applied to a wear-resistant alloy layer of a part with the abrasive wear working condition below 800 ℃, such as a tooth head of a single-roller crusher.
Description
Technical Field
The invention belongs to the technical field of wear-resistant surfacing, and particularly relates to composite powder particles of a titanium carbide (TiC) phase reinforced iron-based surfacing alloy and an application method thereof.
Background
Titanium carbide (TiC) is used as a hard phase with microhardness up to 3200HV and melting point up to 3140 ℃, and is often used as a reinforcing phase in materials such as hard alloy, high temperature alloy and the like. The carbide does not react with air basically at 800 ℃, and has better electrical conductivity and thermal conductivity in metal. TiC is used as a reinforcing phase of the iron-based alloy, has good synchronism with thermal expansion and thermal contraction of a matrix and other phase structures, and has high thermal stability. Thus, TiC is often used as a reinforcing phase and also to adjust the carbide morphology of high chromium alloys and improve their toughness and wear resistance, but rarely as a main wear phase, with the main difficulties: ti belongs to an alloy element with active chemical properties, and the technological problem of meeting the requirements of safety and economy and adding a large amount of Ti cannot be solved.
Industrial TiC powder multipurpose carbon black reduction TiO2The reaction temperature is 1700 ℃ and 2100 ℃, and the reaction is shown as the equation: TiO 22+2C→TiC+CO2. The TiC powder prepared by this reaction is economical. However, the above two-phase TiO2In a closed system with CAnd reaction occurs, and the reaction cannot occur in a multi-component open system environment of a surfacing weld pool. Up to now, no use has been seen (TiO)2Powder + graphite or carbon black) reduction method to prepare TiC phase reinforced iron-based surfacing alloys.
As a wear-resistant alloy with reliable performance and economy, a TiC reinforcing phase contained in the iron-based surfacing alloy is mainly generated in the forms of in-situ precipitation or addition of TiC particles and the like. In-situ TiC phase precipitation needs to add titanium-containing and carbon-containing components such as ferrotitanium and graphite into a welding rod coating or a flux-cored wire, then Ti atoms and C atoms are preferentially combined to precipitate the TiC phase in advance, and the TiC phase precipitation method has the advantage of good combination of the TiC phase and matrix and other tissues. However, the TiC phase particles precipitated in situ are too fine, and generally only have the effects of refining grains and improving the strength and hardness of the alloy, and the effect on improving the wear resistance of the abrasive particles is not obvious. Therefore, a lot of scientists search for technological measures for improving the volume fraction of TiC phase contained in the surfacing alloy. When the amount of TiC added is small, the reaction is similar to that of TiC in-situ precipitation, but the TiC is not ideally combined with a matrix and other structures. The research work of adding a large amount of TiC particles is not greatly developed all the time, and the main symptoms are as follows: and the build-up welding melt with large TiC amount is poor in molding. Because the TiC phase is increased, the fluidity of the surfacing melt is poor, the defects of incomplete fusion, air holes, slag inclusion and the like are easily generated, and the quality of the surfacing alloy is seriously influenced. When submerged arc welding is carried out, slag and surfacing alloy are firmly hardened, and slag removal is extremely difficult, which is mainly caused by that solid-dissolved titanium atoms of the alloy are firmly bonded with crystal lattices such as surface oxides and the like, so that slag removal is difficult. Moreover, the amount of added ferrotitanium or TiC phase is too high, the more the number of released simple substance Ti atoms is, the higher the metallurgical reaction intensity is, the greater the splashing is, the greater the oxidation loss of the titanium component is, and the less the amount of titanium which can be transferred to the alloy is. In view of the above, the amount of TiC phase precipitation is limited in commercial welding materials such as flux-cored wires and flux-cored electrodes, which is the current situation regarding TiC phase-reinforced iron-based overlay alloys.
However, the development of iron-based welding materials such as composite powder particles with the TiC phase as the main wear-resistant phase is still very urgent due to the good properties of the TiC phase under the working condition of medium-high temperature abrasive particles, so that parts under the working condition of wear-resistant particle wear at the temperature of 800 ℃ have economical and reliable surfacing material selection, such as single-roll crusher teeth and other workpieces for crushing hot slag.
Disclosure of Invention
One of the purposes of the invention is to provide composite powder particles of titanium carbide/TiC phase reinforced iron-based surfacing alloy aiming at the defects of the existing welding materials.
The above object of the present invention is achieved by the following technical solutions:
the composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy are prepared into composite powder particles with the particle size of 10-15 meshes by adopting the preparation process steps of sieving and weighing the powder components, dry mixing the powder components, adding water glass into the mixed powder for wet mixing, rotationally bonding and granulating the wet powder, sintering the powder particles at low temperature and sieving the powder particles;
the composite powder particles comprise the following powder components in percentage by weight: 40-50% of titanium carbide powder (TiC) with the titanium carbide content of more than 95%; 12-16% of high-carbon ferrochrome (FeCr70C8.0) with chromium content of 68-72% and carbon content of 8%; 10-15% of ferrotitanium (FeTi70-A) with the titanium content of 70%; 5-7% ferromolybdenum (FeMo50-A) containing 50% of molybdenum; 4-6% of medium carbon ferromanganese (FeMn80C1.5) with manganese content of 78-85% and carbon content of 1.5%; 3-5% of aluminum powder (Al) with the aluminum content not less than 99%; 2-4% of marble powder (CaCO) with calcium carbonate content of more than 99%3) (ii) a 1-3% fluorite powder (CaF) with calcium fluoride content of more than 98.5%2) (ii) a 1-2% zirconium dioxide powder (ZrO) containing more than 99% zirconium dioxide2) (ii) a The balance is reduced iron powder (Fe) with iron content not less than 98%.
Further, the powder components of titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese and reduced iron powder contained in the composite powder particles are sieved by a 60-mesh sieve, and the powder components of aluminum powder, marble powder, fluorite powder and zirconium dioxide powder contained in the composite powder particles are sieved by a 300-mesh sieve and then weighed.
Further, the water glass added to the mixed powder is sodium silicate type, the baume degree is 30-40, and the modulus is 3.0-3.3.
Further, sodium silicate type water glass is added to the mixed powder in a manner of 10 to 15ml of water glass per 100g of the mixed powder, and wet-mixed.
Further, the composite powder particles are sintered at a low temperature of 300-400 ℃, kept warm for 2-4 hours and then discharged from the furnace.
The second object of the invention is to provide an application method of the composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy, which comprises the following steps: the composite powder particles are preset in a weld bead before welding, H08A solid welding wires with the diameter phi of 2.5mm are used as electric arc carriers, submerged arc surfacing is carried out by adopting a direct-current power supply reversal method, the composite powder particle melt and the solid welding wire molten drops are fused into an integrated molten pool, and the molten pool is solidified to form iron-based surfacing alloy with a texture structure which takes blocky or granular titanium carbide/TiC phases as main wear-resistant phases; the powder filling rate (powder filling rate ═ composite powder particle weight/(composite powder particle weight + solid wire melting weight)) of the iron-based surfacing alloy is 0.30-0.40.
Further, the control value of the surfacing current is 440-460A, the traveling speed of the welding seam trolley at the first layer is 11-12 m/h, the traveling speed of the welding seam trolley at the second layer is 12-13 m/h, and the traveling speed of the trolley at the third layer and above the welding seam of the third layer is 13-14 m/h.
Further, the flux used for submerged arc surfacing is SJ 260.
The invention relates to composite powder particles of a titanium carbide phase reinforced iron-based surfacing alloy and an application method thereof. The composite powder particles can be applied to the surfacing of wear-resistant alloy layers of parts with the abrasive wear working condition below 800 ℃, such as the tooth heads of single-roll crushers.
Compared with the prior art, the invention has the following innovation points and beneficial effects:
(1) the main wear-resistant phase is mainly titanium carbide (TiC): the iron-based surfacing alloy prepared by the composite powder particles takes a TiC phase as a main wear-resistant phase, the TiC phase has good compatibility with matrixes such as ferrite, martensite and austenite, the prepared surfacing alloy has no dendritic or reticular eutectic carbide and lamellar or fishbone eutectic and other brittle tissues, has good toughness, and has no cracks seen in more than three layers of preheating surfacing.
(2) Titanium carbide is high in number and large in size: compared with the traditional TiC phase-containing wear-resistant alloy, the composite powder particles are added with 40-50% of TiC powder, the addition amount of the TiC powder is far higher than that of the TiC powder of the flux core or the flux coating of the traditional flux-cored wire, a large amount of TiC particles are separated out from the iron-based alloy of H08A solid welding wire submerged arc surfacing, the volume fraction can reach more than 10-15%, and the TiC phase with the size of 3-8 mu m is much higher than that of the TiC phase with the size of less than 5% and less than 0.2-2 mu m.
(3) The slag removal performance is better: the high-titanium composite powder particles and the solid welding wire are used for preparing the wear-resistant alloy by adopting a submerged arc surfacing process, and the deslagging performance is good. When the traditional submerged arc surfacing welding material such as a flux-cored wire is added with TiC powder with the mass percent of more than 3%, the slag removing property is seriously deteriorated, and the TiC with the mass percent of more than 10% is seriously hardened and cannot be removed. In the invention, a small amount of marble (CaCO) is added into the composite powder particles3) Fluorite (CaF)2) And zirconium dioxide powder (ZrO)2) Etc. wherein CaO decomposed from marble may be reacted with TiO, a Ti component oxide2Compounding into calcium titanate and other slag, and floating out of the surface of the weld seam under the action of electric arc blowing force; CaO can directly remove an oxide layer on the surface of TiC particles to promote complete melting of the TiC particles, so that the TiC particles are completely combined with other phase structures; the added fluorite powder can reduce the intensity of metallurgical reaction of a high-titanium surfacing molten pool, and can play a role in dehydrogenation and improving the toughness of weld metal; with other oxides, e.g. SiO2In contrast, zirconium dioxide (ZrO)2) The thermal stability is high, and the probability of metallurgical reaction between Ti and other oxides can be reduced; at the same time, ZrO2The phase has structural change from high temperature to low temperature to cause volume expansion, and the slag shell can be loosened. In addition, 3-5% of aluminum powder (Al) is added into the composite powder particles, the addition amount is far higher than that of 0.5-1% of Al of a common flux-cored wire or a coated electrode, the oxidation amount of titanium atoms is reduced by utilizing the advanced deoxidation effect of a large amount of aluminum powder, and the slag removal performance is improved by improving the transition coefficient of Ti components.
(4) The wear resistance of the wear-resistant particles is excellent: from the cutting test of the sample grinding wheel, under the action of the same rotating speed and external load, the cutting time of the sample grinding wheel is basically more than 4 times that of the similar high-chromium alloy, and the redder the cutting seam is, the harder the cutting is, and the conventional high-chromium alloy does not have the condition. From the metallographic structure, the notch structure at the beginning basically consists of ferrite, martensite, a small amount of austenite and TiC which are equal, the macroscopic hardness is about 53-56 HRC, and the part of the structure is basically not reddened, namely does not experience the transformation temperature, so the original property is basically maintained; the incision tissue with the red cutting opening comprises austenite, martensite, TiC and the like, and the macroscopic hardness of the alloy is increased to 58-63 HRC; namely, under the action of cutting friction heat, the macroscopic hardness of the composite powder particle surfacing alloy is improved, which shows that the composite powder particle surfacing alloy has excellent high-temperature abrasive wear resistance, and the phenomenon of the wear resistance reduction of the high-chromium alloy along with the temperature increase is obviously different from the phenomenon of the wear resistance reduction of the high-chromium alloy along with the temperature increase.
(5) The TiC phase is precipitated in different processes: in the traditional wear-resistant alloy, TiC is generally formed by melting ferrotitanium components to form Ti atoms which are directly combined with carbon atoms to precipitate a TiC phase; or is formed by incomplete melting of an added TiC phase. Although TiC of the composite powder particle surfacing alloy is added, the TiC phase is firstly melted and decomposed into simple substance Ti and C atoms, then the Ti and C atoms are re-aggregated under the condition of rapid cooling, the TiC phase is compounded and precipitated in situ, the TiC phase is well combined with a matrix and other tissues, and the precipitation of the TiC phase is subjected to the processes of TiC compound decomposition, atom aggregation recombination and the like. Because the precipitation process is obviously different from the traditional mode and the burning loss rates of the Ti and the C components are different, the invention needs to supplement a proper amount of ferrotitanium to make up for the excessive burning loss of titanium atoms, so that the ratio of the Ti atoms to the C atoms reaches the preset balance ratio and is reunited to precipitate as a TiC phase.
Drawings
FIG. 1 is a structural morphology diagram of a TiC phase reinforced iron-based surfacing alloy prepared from the composite powder particles.
FIG. 2 is a phase composition diagram of the TiC phase-reinforced iron-based hardfacing alloy shown in FIG. 1.
FIG. 3 is a wear topography for the TiC phase enhanced iron-based hardfacing alloy of FIG. 1.
FIG. 4 is a structural morphology diagram of an MC phase reinforced iron-based overlay welding alloy prepared by the flux-cored wire of comparative example 1.
FIG. 5 is a phase composition diagram of the MC phase reinforced iron-based overlay alloy of FIG. 4.
FIG. 6 is a wear profile of the MC-phase enhanced iron-based hardfacing alloy of FIG. 4.
Detailed Description
The present invention will be described in further detail with reference to the accompanying drawings and examples.
The invention relates to composite powder particles of a titanium carbide/TiC phase reinforced iron-based surfacing alloy and an application method thereof, which adopts the preparation process steps of sieving and weighing powder components, dry mixing the powder components, adding water glass into the mixed powder for wet mixing, rotationally adhering and granulating the wet powder, sintering the powder particles at low temperature, sieving the powder particles and the like to form the composite powder particles with specific granularity and H08A solid welding wires serving as electric arc carriers as surfacing materials, and carrying out submerged arc surfacing to prepare the iron-based surfacing alloy taking a TiC phase as a main wear-resistant phase;
the mixed powder comprises the following powder components in percentage by weight: 40-50% of titanium carbide powder (TiC) with the titanium carbide content of more than 95%; 12-16% of high-carbon ferrochrome (FeCr70C8.0) with chromium content of 68-72% and carbon content of 8%; 10-15% of ferrotitanium (FeTi70-A) with the titanium content of 70%; 5-7% ferromolybdenum (FeMo50-A) containing 50% of molybdenum; 4-6% of medium carbon ferromanganese (FeMn80C1.5) with manganese content of 78-85% and carbon content of 1.5%; 3-5% of aluminum powder (Al) with the aluminum content not less than 99%; 2-4% of marble powder (CaCO) with calcium carbonate content of more than 99%3) (ii) a 1-3% fluorite powder (CaF) with calcium fluoride content of more than 98.5%2) (ii) a 1-2% zirconium dioxide powder (ZrO) containing more than 99% zirconium dioxide2) (ii) a The balance of reduced iron powder (Fe) with the iron content of not less than 98 percent;
during submerged arc surfacing, the powder filling rate (the powder filling rate is the weight of the composite powder particles/(the weight of the composite powder particles and the melting weight of the solid welding wire)) of the surfacing alloy of the composite powder particles and the H08A solid welding wire is 0.30-0.40, so that the iron-based surfacing alloy with TiC as a main wear-resistant phase is obtained, and the weld metal and the matrix are well fused.
Before weighing the mixed powder components, firstly sieving the powder components such as titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese, reduced iron powder and the like through a 60-mesh sieve, then sieving the powder components such as aluminum powder, marble powder, fluorite powder, zirconium dioxide powder and the like through a 300-mesh sieve, then weighing according to the powder composition proportion of composite powder particles, then putting all the weighed powder components into the same container, and fully stirring to uniformly mix to form mixed powder.
Then, 3-5 ml of sodium silicate type water glass with the Baume degree of 30-40 and the modulus of 3.0-3.3 is added into the mixed powder every time, the water glass and the mixed powder are uniformly infiltrated and fused during the adding process, until the ratio of the added volume of the water glass to the weight of the mixed powder is 10-15 ml of sodium silicate type water glass/100 g of the mixed powder, then the container containing the wet powder is rotated at the speed of 3-6 revolutions per second and slightly vibrated, so that the wet powder rotates and is bonded into composite powder particles, the rotation is stopped until the granularity of most of the composite powder particles in the container is consistent, and the composite powder particles are kept for 15 minutes to be shaped, so that the approximately spherical composite powder particles are obtained.
And then, putting the composite powder particles into a sintering furnace, heating to 300-400 ℃, preserving heat for 2-4 hours, and discharging.
Continuously, sieving the composite powder particles discharged from the furnace by a sieve with 10 meshes, and removing the powder particles larger than 10 meshes; then sieving the powder with a 15-mesh sieve to remove the powder with the particle size less than 15 meshes, and finally obtaining the composite powder with the particle size of 10-15 meshes.
Finally, setting surfacing process parameters of an automatic welding machine on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; H08A solid welding wire with the diameter phi of 2.5mm is used as an electric arc carrier; and (3) presetting the sintered and screened composite powder particles on a welding pass, and adjusting the height and the width of a preset powder particle layer to ensure that the powder filling rate of the composite powder particle surfacing alloy is 0.30-0.40.
Before surfacing, selecting the polarity of an automatic welding machine ZD5-1000E as direct current reverse connection, setting the current value to be 440-460A, the arc voltage to be 26-30V, the dry extension of a welding wire to be 25-30 mm, the travelling speed of a first layer of welding seam trolley to be 11-12 m/h, the travelling speed of a second layer of welding seam trolley to be 12-13 m/h, and the travelling speed of the trolley above a third layer of welding seam and a third layer of welding seam to be 13-14 m/h; and other surfacing process parameters except the trolley travelling speed of each layer are unchanged.
Carrying out submerged arc surfacing by taking the composite powder particles and the H08A solid welding wire as surfacing materials, wherein the used welding flux is SJ260, fusing the composite powder particle melt and the H08A solid welding wire molten drops into an integrated molten pool, forming a first layer of welding seam after the molten pool is air-cooled and solidified, and knocking out surface slag; the second and third layers are then deposited separately in the same manner.
Based on the above, the design principle of the composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy and the application method thereof can be summarized as follows: firstly, preparing 10-15-mesh composite particles, taking the composite particles and a solid welding wire as surfacing materials, optimally configuring components of the composite particles, and regulating and controlling the content of high-carbon ferrochrome to inhibit the precipitation of dendritic or reticular carbides; adding a small amount of ore powder with high chemical stability to regulate and control the reaction intensity of a surfacing molten pool, removing oxides and loosening slag shells; adding a large amount of strong deoxidizer aluminum powder to reduce the oxidation amount of titanium atoms; adding a proper amount of ferromolybdenum to improve the heat resistance of the surfacing alloy and increase the diffusion speed of carbon atoms in a molten pool so that a large amount of carbon atoms required for separating out a TiC phase can be supplied in time; adding a proper amount of ferromanganese to increase the toughness of the welding seam and improve the macroscopic hardness of the welding seam; supplementing a proper amount of ferrotitanium components to make up for excessive burning loss of the titanium components; adopting higher surfacing current 440-460A, controlling welding speed in a layered mode, completely melting the added TiC particles, and then aggregating, precipitating and growing in situ, so that the TiC particles are firmly combined with tissues such as a matrix; the comprehensive effect of the measures enables the chemical components of the surfacing molten pool to meet the requirements of a large amount of instantaneous precipitation conditions of TiC phases, the actual surfacing process and the economy, thereby forming the iron-based surfacing alloy taking the TiC phases as the main wear-resistant phases.
Example 1
Before weighing, powder components of titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese and reduced iron powder are sieved by a 60-mesh sieve, and powder components of marble powder, fluorite powder, zirconium dioxide powder and aluminum powder are sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 50% of titanium carbide powder, 12% of high-carbon ferrochrome, 12% of ferrotitanium, 6% of ferromolybdenum, 6% of medium-carbon ferromanganese, 5% of aluminum powder, 4% of marble powder, 1% of fluorite powder, 1% of zirconium dioxide powder and 3% of reduced iron powder. Weighing the powder components such as titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese, aluminum powder, marble powder, fluorite powder, zirconium dioxide powder, reduced iron powder and the like according to the composition proportion requirements of the powder components contained in the composite powder, then putting all the weighed powder components into a same container, and fully stirring to uniformly mix the weighed powder components to form mixed powder.
Then, 3-5 ml of sodium silicate type water glass with Baume degree of 40 and modulus of 3.0 is added into the mixed powder every time, stirring is continuously carried out during the adding process to enable the water glass and the mixed powder to be evenly soaked and fused until 12ml of sodium silicate type water glass with volume is finally added into 100g of the mixed powder; then rotating at the speed of 3-6 revolutions per second, slightly vibrating the container containing the wet mixed powder to rotate and bond the wet mixed powder into composite powder particles, continuously rotating until the granularity of most of the composite powder particles in the container is consistent, and standing for 15 minutes to shape to obtain approximately spherical composite powder particles;
and continuously putting the composite powder particles into a sintering furnace, heating to 320 ℃, preserving the heat for 4 hours, and discharging. Then, the sintered composite powder particles are firstly screened by a 10-mesh sieve, and large particles larger than 10 meshes are removed; and sieving the powder by a 15-mesh sieve to remove small particles smaller than 15 meshes, and finally obtaining the composite powder with the granularity of 10-15 meshes.
Finally, H08A solid welding wires with the diameter of phi 2.5 are adopted as electric arc carriers on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; the screened composite powder particles are preset in a weld bead, and the height and the width of a preset powder particle layer are optimally adjusted, so that the powder filling rate of the surfacing alloy is 0.35.
Before surfacing, the polarity of the automatic welding machine ZD5-1000E is set to be direct current reverse connection, and surfacing process parameters are shown in Table 1. Wherein the travelling speed of the trolley for the welding seams at the first layer is 11-12 m/h, the travelling speed of the trolley for the welding seams at the second layer is 12-13 m/h, and the travelling speed of the trolley for the welding seams at the third layer and above the third layer is 13-14 m/h; and other surfacing process parameters except the trolley travelling speed of each layer are unchanged.
TABLE 1 composite powder and solid wire submerged-arc build-up welding process parameters
And (3) performing submerged arc surfacing by using the sintered and sieved composite powder particles and H08A solid welding wires as surfacing materials, wherein the used welding flux is SJ260, and fusing the composite powder particle melt and the solid welding wire molten drops into an integrated molten pool. Removing surface slag after a first layer of welding seam is formed by air cooling and solidification of a molten pool; then, the second layer and the third layer are each built up in the same manner. After welding, the welding seam has no defects of cracks, air holes and the like.
The surfacing test piece is processed by a wire cutting method to prepare a wear-resistant test piece with the thickness of 57mm multiplied by 25.5mm multiplied by 6mm, and the macroscopic hardness of the surface of the wear-resistant test piece is tested by an HR-150 Rockwell hardness tester.
The wear resistance test adopts an MLS-225B type wet sand rubber wheel type wear testing machine, and the test conditions are as follows: the diameter of the rubber wheel is 176mm, the hardness is 60 Shore, the weight is 2.5 kg, the rotating speed of the rubber wheel is 240 r/min, and the proportion of the mortar is 1500 g of quartz sand of 40-60 meshes and 1000 g of tap water. Pre-grinding a sample for 1000 turns, washing, drying, and weighing the initial weight M0Then the mixture is cleaned and dried after 1000 turns in a formal test, and weighed M1The absolute weight loss of the sample (delta M) is M0-M1。
The following 1# surfacing test sample described in relation to the proportion 1 was used as a standard sample, and the relative wear coefficient ∈ was the absolute weight loss of the standard sample/absolute weight loss of the sample, and the test results are shown in table 2.
The structure, phase composition and wear morphology of the overlay welding alloy of the embodiment 1 are shown in the attached fig. 1, the attached fig. 2 and the attached fig. 3 respectively.
Example 2
Before weighing, powder components of titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese and reduced iron powder are sieved by a 60-mesh sieve, and powder components of aluminum powder, marble powder, fluorite powder and zirconium dioxide powder are sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 40% of titanium carbide powder, 14% of high-carbon ferrochrome, 13% of ferrotitanium, 7% of ferromolybdenum, 5% of medium-carbon ferromanganese, 4% of aluminum powder, 3% of marble powder, 1.5% of fluorite powder, 1% of zirconium dioxide powder and 11.5% of reduced iron powder. Weighing the powder components such as titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese, aluminum powder, marble powder, fluorite powder, zirconium dioxide powder, reduced iron powder and the like according to the composition proportion requirements of the powder components contained in the composite powder, then putting all the weighed powder components into a same container, and fully stirring to uniformly mix the weighed powder components to form mixed powder.
Then, 3-5 ml of sodium silicate type water glass with Baume degree of 40 and modulus of 3.0 is added into the mixed powder every time, stirring is continuously carried out during the adding process to enable the water glass and the mixed powder to be evenly soaked and fused until 14ml of sodium silicate type water glass with volume is finally added into 100g of the mixed powder; then rotating at the speed of 3-6 revolutions per second, slightly vibrating the container containing the wet mixed powder to rotate and bond the wet mixed powder into composite powder particles, continuously rotating until the granularity of most of the composite powder particles in the container is consistent, and standing for 15 minutes to shape to obtain approximately spherical composite powder particles;
and continuously putting the composite powder particles into a sintering furnace, heating to 330 ℃, keeping the temperature for 3 hours, and discharging. Then, the sintered composite powder particles are firstly screened by a 10-mesh sieve, and large particles larger than 10 meshes are removed; and sieving the powder by a 15-mesh sieve to remove small particles smaller than 15 meshes, and finally obtaining the composite powder with the granularity of 10-15 meshes.
Finally, H08A solid welding wires with the diameter of phi 2.5 are adopted as electric arc carriers on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; the screened composite powder particles are preset in a weld bead, and the height and the width of a preset powder particle layer are optimally adjusted, so that the powder filling rate of the surfacing alloy is 0.39.
The remaining steps and the abrasion resistance test were the same as in example 1.
Example 3
Before weighing, powder components of titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese and reduced iron powder are sieved by a 60-mesh sieve, and powder components of aluminum powder, marble powder, fluorite powder and zirconium dioxide powder are sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 45% of titanium carbide powder, 16% of high-carbon ferrochrome, 10% of ferrotitanium, 5% of ferromolybdenum, 4% of medium-carbon ferromanganese, 5% of aluminum powder, 4% of marble powder, 2% of fluorite powder, 1.5% of zirconium dioxide powder and 7.5% of reduced iron powder. Weighing the powder components such as titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese, aluminum powder, marble powder, fluorite powder, zirconium dioxide powder, reduced iron powder and the like according to the composition proportion requirements of the powder components contained in the composite powder, then putting all the weighed powder components into a same container, and fully stirring to uniformly mix the weighed powder components to form mixed powder.
Then, 3-5 ml of sodium silicate type water glass with Baume degree of 40 and modulus of 3.0 is added into the mixed powder every time, stirring is continuously carried out during the adding process to enable the water glass and the mixed powder to be evenly soaked and fused until 12ml of sodium silicate type water glass with volume is finally added into 100g of the mixed powder; then rotating at the speed of 3-6 revolutions per second, slightly vibrating the container containing the wet mixed powder to rotate and bond the wet mixed powder into composite powder particles, continuously rotating until the granularity of most of the composite powder particles in the container is consistent, and standing for 15 minutes to shape to obtain approximately spherical composite powder particles;
continuously putting the composite powder particles into a sintering furnace, heating to 360 ℃, keeping the temperature for 2.5 hours, and discharging; then, the sintered composite powder particles are firstly screened by a 10-mesh sieve, and large particles larger than 10 meshes are removed; and sieving the powder by a 15-mesh sieve to remove small particles smaller than 15 meshes, and finally obtaining the composite powder with the granularity of 10-15 meshes.
Finally, H08A solid welding wires with the diameter of phi 2.5 are adopted as electric arc carriers on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; the screened composite powder particles are preset in a weld bead, and the height and the width of a preset powder particle layer are optimally adjusted to enable the powder filling rate of the surfacing alloy to be 0.37.
The remaining steps and the abrasion resistance test were the same as in example 1.
Comparative example 1
The MC phase reinforced iron-based surfacing alloy is formed by submerged arc surfacing of a self-made flux-cored wire, the H08A cold-rolled thin steel strip (the width is 16mm multiplied by the thickness is 0.36mm) is used as an outer layer wrapper, powder components are matched in the wrapper to form a powder core, and the powder core comprises the following components: 20% of high-carbon ferrochrome, 30% of medium-carbon ferromanganese, 5% of FeV50-A type ferrovanadium, 5% of FeB18 type ferroboron, 8% of FeNb60-A type ferroniobium, 3% of graphite, 3% of titanium carbide powder, 6% of FeSi45-A type ferrosilicon and 20% of reduced iron powder (note: the powder components of the unmarked type are the same as the corresponding powder types adopted by the composite powder particles of the invention); the filling rate of the flux-cored wire is 45%.
The setting of the walking speed of each layer of trolley is 13-14 m/h, and only a flux-cored wire is used as a surfacing material, and other surfacing process parameters, polarity setting and surfacing processes of the automatic welding machine ZD5-1000E used in the comparative example 1 are the same as those in the example 1. The abrasion resistance test was conducted in the same manner as in example 1.
The structure morphology and the phase composition of the MC-phase reinforced iron-based surfacing alloy shown in comparative example 1 are shown in fig. 4 and 5, respectively, the wear morphology of the surfacing alloy prepared in comparative example 1 is shown in fig. 6, and the MC-phase reinforced iron-based surfacing alloy prepared in comparative example 1 is used as a # 1 comparative sample.
As can be seen from Table 2, the relative wear coefficient epsilon of the TiC reinforced iron-based surfacing alloy prepared by the composite particles is 2.10-2.67 times that of the MC phase reinforced iron-based surfacing alloy prepared in the comparative example 1, which shows that the TiC phase reinforced iron-based surfacing alloy prepared by the composite particles has excellent wear resistance.
TABLE 2 abrasion resistance of wear resistant particles of iron-based overlay alloys prepared in comparative examples and examples
As can be seen from the attached drawings 1 and 2, the structure of the submerged arc surfacing alloy taking the composite powder particles and the H08A solid welding wire as welding materials mainly comprises ferrite, martensite, TiC phases and a small amount of austenite. Wherein, the volume fraction of the TiC phase reaches more than 10-15%, the size is 3-8 μm, and the TiC phase is much higher than that of the TiC phase with the volume fraction of less than 5% and the size of 0.2-2 μm.
In addition, as shown in the attached figure 2, TiC contained in the surfacing alloy prepared by the method is granular and is uniformly dispersed, the structure does not have a traditional lamellar or honeycomb brittle eutectic structure, the macroscopic hardness of the surfacing alloy is about 53-56 HRC, three layers of preheating surfacing are not generated, and cracks are not generated.
In contrast, the cost of the surfacing alloy material of the comparative example 1 is close to that of the embodiment 1, but the preparation cost is higher, and the surfacing process parameters are basically the same. As can be seen from FIGS. 4 and 5, the structure of the weld deposit alloy prepared in comparative example 1 consists of austenite gamma-Fe in a cellular form, and (Fe, Cr) distributed along a cellular crystal network or in a dendritic form23C6And MC is precipitated in the crystal, wherein M comprises elements such as Nb and V, and the structural balance of the alloy is obviously poorer than that of the surfacing alloy prepared by the invention. Due to the large amount of intergranular network or dendrite (Fe, Cr) as shown in comparative example 123C6The surfacing alloy is obviously brittle compared with the surfacing alloy prepared by the composite powder particles.
Comparing the wear profiles of the two iron-based surfacing alloys shown in the attached drawings 3 and 6, the number of scratches on the surface of the surfacing alloy prepared by the two methods is basically similar under the same abrasive wear test condition, but many scratches shown in the attached drawing 3 are stopped when meeting a particle phase, but have plastic deformation traces; fig. 6 shows that the scratch has substantially no discontinuity and no trace of plastic deformation. The abrasion mechanisms of the two are micro-cutting of abrasive particles, but the surfacing alloy prepared by surfacing of the composite particles has better toughness, and although the matrix of the comparative example 1 is mainly austenite, the matrix has higher toughness.
From the cutting test of the grinding wheel, under the same conditions, the cutting time of the iron-based surfacing alloy prepared by the composite powder particles is about 4 times or more than that of the iron-based surfacing alloy in the comparative example 1, which shows that the iron-based surfacing alloy has excellent high-temperature abrasive wear resistance.
The results show that the TiC phase reinforced surfacing alloy prepared by the composite powder particles has good wear resistance and higher toughness, and the composite powder particles can be applied to a part surfacing wear-resistant alloy layer under the abrasive wear working condition below 800 ℃, such as a tooth head of a single-roll crusher, can be matched with an H08A solid welding wire for use, and can also be independently used for welding materials for deposition such as TiG and the like.
Claims (8)
1. The composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy are characterized in that: the preparation method comprises the following steps of screening and weighing powder components, dry-mixing the powder components, adding water glass into the mixed powder, wet-mixing, carrying out rotary bonding granulation on the wet powder, sintering the powder particles at a low temperature, and screening the powder particles to prepare composite powder particles with the particle size of 10-15 meshes;
the composite powder particles comprise the following powder components in percentage by weight: 40-50% of titanium carbide powder with titanium carbide content of more than 95%; 12-16% of high-carbon ferrochrome with 68-72% of chromium content and 8% of carbon content; 10-15% of ferrotitanium with 70% of titanium content; 5-7% of ferromolybdenum with 50% of molybdenum content; 4-6% of medium carbon ferromanganese with manganese content of 78-85% and carbon content of 1.5%; 3-5% of aluminum powder with aluminum content not less than 99%; 2-4% of marble powder with calcium carbonate content of more than 99%; 1-3% of fluorite powder with calcium fluoride content of more than 98.5%; 1-2% of zirconium dioxide powder with zirconium dioxide content of more than 99%; the rest is reduced iron powder with iron content not less than 98%.
2. The composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy according to claim 1, wherein the composite powder particles are prepared by mixing the following raw materials in parts by weight: the powder components of titanium carbide powder, high-carbon ferrochrome, ferrotitanium, ferromolybdenum, medium-carbon ferromanganese and reduced iron powder contained in the composite powder particles are sieved by a 60-mesh sieve, and the powder components of aluminum powder, marble powder, fluorite powder and zirconium dioxide powder contained in the composite powder particles are sieved by a 300-mesh sieve and then weighed.
3. The composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy according to claim 1, wherein: the water glass added to the mixed powder is sodium silicate, the Baume degree is 30-40, and the modulus is 3.0-3.3.
4. The composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy according to claim 1, wherein the composite powder particles are prepared by mixing the following raw materials in parts by weight: the water glass is added to the mixed powder in a manner of 10-15 ml of sodium silicate type water glass per 100g of the mixed powder, and wet mixing is performed.
5. The composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy according to claim 1, wherein the composite powder particles are prepared by mixing the following raw materials in parts by weight: sintering the composite powder particles at a low temperature of 300-400 ℃, preserving heat for 2-4 hours, and discharging.
6. A method of applying composite powder particles of the titanium carbide phase reinforced iron-based overlay alloy according to claim 1, characterized in that: the composite powder particles are preset in a weld bead before welding, H08A solid welding wires with the diameter phi of 2.5mm are used as electric arc carriers, submerged arc surfacing is carried out by adopting a direct-current power supply reversal method, the composite powder particle melt and the solid welding wire melt drops are fused into an integrated molten pool, and an iron-based surfacing alloy with a texture structure taking a massive or granular titanium carbide phase as a main wear-resistant phase is formed by solidification; the powder filling rate of the iron-based surfacing alloy is equal to the weight of composite powder particles/(the weight of the composite powder particles and the melting weight of the solid welding wire), and the powder filling rate is 0.30-0.40.
7. The method for applying the composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy according to claim 6, wherein the method comprises the following steps: the control value of the surfacing current is 440-460A, the traveling speed of the welding seam trolley at the first layer is 11-12 m/h, the traveling speed of the welding seam trolley at the second layer is 12-13 m/h, and the traveling speed of the trolley at the third layer and above the welding seam at the third layer is 13-14 m/h.
8. The method for applying the composite powder particles of the titanium carbide phase reinforced iron-based surfacing alloy according to claim 6, wherein the method comprises the following steps: the flux used for submerged arc surfacing is SJ 260.
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| CN114535567B (en) * | 2021-12-14 | 2023-09-01 | 湘潭大学 | Composite powder particle of high-vanadium high-boron alloy for surfacing and application method thereof |
| CN114055015B (en) * | 2021-12-20 | 2022-11-25 | 湘潭大学 | Self-protection open arc surfacing flux-cored wire and application method thereof |
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| US5038640A (en) * | 1990-02-08 | 1991-08-13 | Hughes Tool Company | Titanium carbide modified hardfacing for use on bearing surfaces of earth boring bits |
| CN101602150B (en) * | 2009-07-15 | 2011-08-17 | 中天仕名科技集团有限公司 | Impact abrasion resistant flux-cored wire used for hammer head of hammer crusher |
| CN101837523B (en) * | 2010-06-11 | 2013-12-11 | 河海大学常州校区 | Titanium reinforced wear-resistance submerged overlaying flux-cored wire |
| CN104493375A (en) * | 2014-10-31 | 2015-04-08 | 河海大学常州校区 | Titanium-reinforced hardfacing electrode and manufacturing method thereof |
| CN104625487B (en) * | 2015-02-12 | 2017-01-11 | 西安理工大学 | Reinforced abrasion-resistant surface welding flux-cored wire made of in-situ generated titanium carbide and method for manufacturing reinforced abrasion-resistant surface welding flux-cored wire |
| CN110385547B (en) * | 2019-09-18 | 2019-12-10 | 东营威玛石油钻具有限公司 | Wear-resistant surfacing flux-cored wire for thin-diameter petroleum drilling tool |
| CN110549035B (en) * | 2019-10-14 | 2021-02-26 | 湘潭大学 | Composite powder of submerged arc surfacing high-boron alloy and application method thereof |
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