CN115740833A - Composite powder particle for surfacing drill rod wear-resistant belt and application method - Google Patents
Composite powder particle for surfacing drill rod wear-resistant belt and application method Download PDFInfo
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Abstract
The composite powder particles for the wear-resistant belt of the surfacing drill rod joint are prepared into composite powder particles with the particle size of 8-10 meshes by adopting 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, rotating wet powder for bonding and granulating, sintering the powder particles at low temperature, sieving the powder particles and the like. And then, taking the composite powder particles and the H08A solid welding wire as surfacing materials, and carrying out submerged arc surfacing so that the composite powder particle melt and the solid welding wire are molten and fused into a surfacing molten pool and solidified into medium chromium alloy. Regulating and controlling the alloy component variety and content of the composite powder particles to optimize the content of carbon atoms and chromium atoms in cellular crystal and crystal boundary regions; at the same time, the modification of eutectic and along-grain carbide morphology by Ti and Nb is utilized to form (Nb, ti) C and fine particles (Fe, cr) 3 C phase-strengthened acicular ferrite cellular group and (Fe, cr) 7 C 3 Medium chromium with structure of grains arranged as network phase along cellular grain boundaryThe alloy fully utilizes different functions of various phase structures to obtain excellent wear resistance. The composite powder particles can be used for surfacing of wear-resistant alloy layers of parts under abrasive wear conditions, such as wear-resistant belts of petroleum drill pipe joints.
Description
Technical Field
The invention belongs to the technical field of wear-resistant surfacing, and particularly relates to composite particles of a wear-resistant belt of a surfacing drill rod joint and an application method thereof.
Background
When the petroleum drilling rod is used for drilling, the joints of the petroleum drilling rod are subjected to abrasive wear with soil, rock gravel and the like around the drill hole, and a wear-resistant strip needs to be overlaid on the surfaces of the joints of the petroleum drilling rod to ensure the service life of the petroleum drilling rod. However, the end-to-end arc welding mode of the circumferential weld generates large stress, and transverse cracks and the like are easily generated at the ending part and adjacent areas. However, the large tangential stress generated during the screwing operation causes the crack to expand to the drill rod body, thereby affecting the service life of the drill rod. Therefore, the toughness of the wear-resistant belt of the drill rod joint is required to be improved, and the wear-resistant belt of the drill rod joint is required to have high abrasive particle grinding resistance.
At present, the mainstream method for surfacing the wear-resistant belt of the drill rod joint is flux-cored welding carbon dioxide gas shielded welding, the specification of the used welding wire is mostly phi 1.6mm, the powder filling amount is about 25%, and the actually filled alloy powder amount is limited, so that an alloy system for surfacing the wear-resistant belt is greatly limited, and a wear-resistant alloy with good wear resistance and toughness is difficult to obtain. Generally, the greatest effect on the wear resistance of an alloy is the volume fraction of its hard phase, such as carbides, borides. Among them, borides are generally brittle and are more prone to cracking during surfacing, and although their economy and wear resistance of wear-resistant particles are better, their toughness is insufficient, so that their practical application is limited. At present, the surfacing alloy structure is mostly a mixed matrix of acicular martensite and austenite, wherein a small amount of small-particle MC type reinforcements are mixed, the alloy toughness is enough, but many MC particles are small, and some phases are like Fe 3 C is hardly utilized, the abrasive wear resistance of the alloy has a larger room for improvement, and the structural structure of the alloy still needs to be improved so as to optimize the wear resistance. Moreover, the lead time and the production time of the flux-cored wire are too long, the flux-cored wire with the diameter of 1.6mm is not a mainstream device in the market, and the lead time and the production cost are too few, but the flux-cored wire with the diameter of 1.6mm is suitable for welding materials for robots, and is difficult to supply in time and high in preparation cost in case of emergency.
In addition, the method for overlaying the wear-resistant drill rod joint comprises the following steps: MIG welding, plasma arc welding and laser welding, wherein the filling material used by MIG welding is a flux-cored wire, and although the argon protection mode is inert compared with carbon dioxide gas shielded welding, the welding quality is high, but the cost is higher, and the industrial application is less. The filling material used for plasma arc welding and laser welding is atomized powder, special development is needed, and because the energy density of plasma arc and laser is too high, the cooling solidification is fast, although the hardness of deposited alloy is higher due to grain refinement, the surface of a welding seam is easy to crack due to too high residual thermal stress. Secondly, the deposition efficiency is lower than that of the flux-cored wire gas shielded welding.
Disclosure of Invention
One of the objects of the present invention is to provide composite particles for overlaying a wear-resistant strip of a tool joint.
The above object of the present invention is achieved by the following technical solutions:
the composite powder particles are prepared into composite powder particles with the particle size of 8 meshes to 10 meshes by the preparation process steps of weighing and sieving the powder components, dry mixing, adding water glass for wet mixing, bonding and granulating, sintering at low temperature and sieving the powder particles;
the composite powder particles comprise the following powder components in percentage by weight: high-carbon ferrochrome (FeCr70C 8.0) with 48-50% of chromium content of 68-72% and 8% of carbon content; 23-25% ferroniobium (FeNb 60-A) containing 60% niobium; 10-12% of flake graphite (C) with carbon content not less than 98%; 4-6% of medium carbon ferromanganese (FeMn80C1.5) with manganese content of 78-85% and carbon content of 1.5%; 4-5% of ferrotitanium (FeTi 30-A) with the titanium content of 25-35%; 2-3% ferrosilicon (FeSi 45-A) containing 40-47% of silicon; 2-3% of aluminum powder (Al) with the aluminum content not less than 99%; the balance is reduced iron powder (Fe) with iron content not less than 98%.
Further, the powder components of high-carbon ferrochrome, ferrocolumbium, flake graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon and reduced iron powder contained in the composite powder particles are sieved by a 60-mesh sieve, and the powder components of the aluminum powder are sieved by a 300-mesh sieve and then weighed.
Furthermore, the water glass added into the mixed powder is sodium silicate type, the Baume degree is 30-40, and the modulus is 3.0-3.3.
Further, water glass was added to the mixed powder so as to wet mix 20 to 25ml of sodium silicate type water glass per 100g of the mixed powder.
Further, the composite powder particles are sintered at a low temperature of between 250 and 350 ℃ and are discharged after heat preservation for 2 to 4 hours.
The second object of the present invention is to provide a method for applying the composite powder, which comprises: the composite powder particles are preset in a weld bead before welding, H08A solid welding wire with the diameter phi of 2.5mm is used as an arc carrier, submerged arc surfacing is carried out by adopting a direct-current power supply reverse connection method, the composite powder particle melt and the solid welding wire are fused into a surfacing molten pool, and the (Nb, ti) C-phase reinforced medium chromium alloy with the powder filling rate (the powder filling rate = composite powder particle melting weight/(composite powder particle melting weight + solid welding wire melting weight)) of 0.27-0.30 and the macroscopic hardness of more than 57HRC is obtained.
Further, the control value of the surfacing current is 410-420A, and the travelling speed of the welding machine trolley is 15-16 m/h.
Further, the flux for submerged arc surfacing is a melting flux HJ260.
The invention relates to a composite powder particle, which is used together with an H08A solid welding wire, a wear-resistant alloy prepared by overlaying belongs to a medium chromium alloy, and a wear-resistant phase of the wear-resistant alloy comprises a (Nb, ti) C phase precipitated in situ in cellular crystal and (Fe, cr) distributed along the cellular crystal boundary 7 C 3 The two phases cooperate with each other to synergistically improve the wear resistance of the alloy. The medium chromium alloy presents a typical hypoeutectic structure and can be applied to a wear-resistant alloy layer of parts in the abrasive wear working condition, such as a wear-resistant belt of an oil drill pipe joint.
Compared with the prior art, the invention has the following innovation points and beneficial effects:
(1) The wear resistance is excellent: compared with the wear-resistant alloy with a hypoeutectic structure and the wear-resistant alloy reinforced by the NbC phase, the wear-resistant phase of the surfacing alloy comprises (Nb, ti) C phase precipitated in situ in acicular ferrite clusters and granular (Fe, cr) distributed along the crystals 7 C 3 Phase composition, firstly, the cellular crystal is mainly acicular ferrite group, and a large amount of granular (Fe, cr) is mixed in the cellular crystal 3 C phase and bulk (Nb, ti) C phase, which gives it good toughness. (Nb, ti) C phase precipitated in situ in the cellular crystal, granular (Fe, cr) distributed along the cellular grain boundary 7 C 3 Phase-and cellular intragranular (Fe, cr) 3 The C phase is distributed in different areas of the cellular crystal respectively, and the abrasive particles are not easy to wedge due to the synergistic strengthening effectThereby having excellent wear resistance.
(2) Morphology along the crystal carbides differs: with network or dendrites (Fe, cr) generally distributed along the cell-like crystal 7 C 3 Phase or (Fe, cr) 7 (C,B) 3 The difference is that the mesomorphic carbide of the medium chromium alloy of the composite powder bead weld of the invention is not distributed in a whole block because the granular carbide is arranged along cellular grain boundaries although the mesomorphic carbide presents a net shape or a dendritic crystal in shape, and does not have the super-strong rigidity of the whole block of mesomorphic carbide, so that the mesomorphic carbide has better toughness, simultaneously also has proper rigidity to present higher crack resistance, and does not generate any crack in two layers of bead weld under the state before prehot welding.
(3) The surfacing method is simple and quick: compared with a flux-cored wire gas shielded welding method for the wear-resistant belt of the petroleum drill pipe joint, the method for performing submerged arc surfacing on the wear-resistant belt of the petroleum drill pipe joint by using the composite powder particles and the H08A solid welding wire is simple, the equipment investment is low, the composite powder particles are prepared quickly, the alloy system and the component content of the wear-resistant belt can be adjusted in time as required, and the wear-resistant belt alloy with more excellent performance is prepared.
(4) The welding seam shaping is pleasing to the eye and melt and apply efficiently: the medium chromium composite powder of the invention does not add a large amount of Ti-containing components, and compared with a high titanium flux-cored wire, the submerged arc welding seam of the composite powder is beautiful in forming, smooth in surface and free from the defects of slag adhesion, cracks and the like. In addition, the formula can be directly converted into a flux-cored wire formula with the diameter phi of 1.6mm, the gas shielded welding seam is also attractive in forming, and seamless connection from composite powder particles to the flux-cored wire can be directly realized. Because the surfacing current of the composite powder particles is usually over 400A and is far larger than the current value of about 200A of the flux-cored wire gas shielded welding with phi 1.6mm, the metal deposition amount in unit time is larger, and the deposition efficiency is high.
Drawings
FIG. 1 is a structural morphology of a chromium alloy prepared from the composite powder particles of the present invention.
FIG. 2 is a phase composition diagram of the chromium alloy shown in FIG. 1.
FIG. 3 is a structural morphology of the composite powder particle overlay alloy shown in comparative example 1.
FIG. 4 is a phase composition diagram of the overlay alloy of comparative example 1 shown in FIG. 3.
FIG. 5 is a wear profile of the hardfacing alloy of FIG. 1.
FIG. 6 is a wear profile of the overlay alloy of comparative example 1 shown in FIG. 3.
Detailed Description
The present invention will be described in further detail with reference to the accompanying drawings and examples. But the embodiments of the present invention are not limited thereto.
The composite powder particles are prepared into composite powder particles with the particle size of 8-10 meshes by the preparation process steps of weighing and sieving the powder components, dry mixing, adding water glass for wet mixing, adhering and granulating, sintering at low temperature and sieving the powder particles;
the composite powder particles comprise the following powder components in percentage by weight: high-carbon ferrochrome (FeCr70C 8.0) with 48-50% of chromium content of 68-72% and 8% of carbon content; 23-25% of ferrocolumbium (FeNb 60-A) containing 60% of niobium; 10-12% of flake graphite (C) with carbon content not less than 98%; 4-6% of medium carbon ferromanganese (FeMn80C1.5) with manganese content of 78-85% and carbon content of 1.5%; 4-5% of ferrotitanium (FeTi 30-A) with the titanium content of 25-35%; 2-3% of ferrosilicon (FeSi 45-A) with silicon content of 40-47%; 2-3% of aluminum powder (Al) with the aluminum content not less than 99%; the balance is reduced iron powder (Fe) with iron content not less than 98%.
Before weighing the components, powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, reduced iron powder and the like are sieved by a 60-mesh sieve, then aluminum powder is sieved by a 300-mesh sieve, then weighing is carried out according to the composition proportion, and then all the powder components are put into the same container and fully stirred to be uniformly mixed to form mixed powder.
Adding 5ml of sodium silicate type water glass with the Baume degree of 30-40 and the modulus of 3.0-3.3 into the mixed powder every time until each 100g of the mixed powder finally contains 20-25 ml of water glass; during the addition, stirring is not stopped, the mixed powder is evenly soaked by the water glass, then the container is shaken to rotate the wet powder to form spheroidal wet powder particles, and the powder is stood for more than 10 minutes to be shaped.
And continuously placing the spheroidal wet composite powder particles into a sintering furnace, heating to 250-350 ℃, preserving heat for 2-4 hours, cooling to room temperature along with the furnace, and discharging.
Then, the sintered composite powder particles are sieved by an 8-mesh sieve, and large particles larger than 8 meshes are removed; then the powder is sieved by a 10-mesh sieve, and small particles smaller than 10 meshes are removed, so that composite powder particles with the particle size of 8-10 meshes are finally obtained.
The composite powder particles are preset on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16mm, an H08A solid welding wire with the diameter of phi 2.5 is used as an electric arc carrier, and the height and the width of the preset powder particle layer are optimally adjusted on the premise of ensuring good fusion of the surfacing alloy and a substrate, so that the surfacing alloy with the powder filling rate of 0.27-0.30 is obtained.
Before surfacing, the polarity of an automatic welding machine ZD5-1000E is set as direct current reverse connection, the current setting value is 410-420A, the arc voltage is 25-30V, the dry extension of a welding wire is 25-30 mm, the travelling speed of a trolley is 15-16 m/h, and the technological parameters of each layer of surfacing are unchanged.
Carrying out submerged-arc welding by taking the composite powder particles and the H08A solid welding wire as surfacing materials, fusing the composite powder particle melt and the H08A solid welding wire molten drops into a surfacing molten pool, forming a first layer of welding seam after the molten pool is cooled and solidified, and cooling the first layer of welding seam to room temperature to ensure that molten slag on the surface of the welding seam automatically falls off; a second layer is then built up in the same manner.
Based on the above, the design principle of the composite powder particles for overlaying the wear-resistant belt of the drill rod joint and the application method thereof can be summarized as follows: firstly, preparing composite powder particles with the granularity of 8-10 meshes, and then carrying out submerged arc surfacing by taking the composite powder particles and an H08A solid welding wire as surfacing materials so as to fuse a composite powder particle melt and the solid welding wire into a surfacing molten pool and solidify the composite powder particle melt and the solid welding wire into medium chromium alloy; meanwhile, the variety and the content of alloy components of composite powder particles are optimized and regulated, the carbon atom and chromium atom contents in cellular intragranular and grain boundary regions are optimized and regulated by utilizing the Mn capability of stabilizing primary austenite and the function of adjusting the diffusion speed of carbon atoms by silicon components, the primary cellular austenite is poor in carbon and unstable to generate structure transformation by combining with the in-situ precipitation strengthening of (Nb, ti) C, and the modification effect of the Ti and Nb components on eutectic and along-crystal carbide forms is fully utilized, so that (Nb, ti) C and fine particles (F, ti) are formede,Cr) 3 C phase-strengthened acicular ferrite cellular group and (Fe, cr) 7 C 3 The medium chromium alloy with the structure that the grains are arranged into a net phase along cellular grain boundaries fully utilizes different functions of various phase structures in the medium chromium alloy to improve the wear resistance of the alloy.
Example 1
Before weighing the components, powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, reduced iron powder and the like are sieved by a 60-mesh sieve, and then aluminum powder is sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 48% of high-carbon ferrochromium, 24% of ferroniobium, 12% of flake graphite, 5% of medium-carbon ferromanganese, 5% of ferrotitanium, 3% of ferrosilicon, 2% of aluminum powder and 1% of reduced iron powder.
Weighing powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, aluminum powder, reduced iron powder and the like according to the composition proportion of the composite powder particles, then putting all the weighed powder components into the same container, and fully stirring to mix uniformly to form mixed powder.
Then, 5ml of sodium silicate type water glass with the Baume degree of 30 and the modulus of 3.3 is added into the mixed powder each time, stirring is continuously carried out during the adding period, so that the water glass is evenly soaked into the mixed powder, and the water glass with the volume of 20ml is finally added into each 100g of the mixed powder; then rotating the container at a speed of 4-6 revolutions per second to rotate the wet mixed powder and bond the wet mixed powder into composite powder particles; meanwhile, mashing large particles, slightly vibrating the container up and down, then rotating the container until the particle sizes of most of the composite particles are consistent, and standing for 10 minutes for shaping to obtain approximately spherical composite particles;
and continuously putting the composite powder particles into a sintering furnace, heating to 290 ℃, preserving heat for 3 hours, and discharging. Then, the sintered composite powder particles are sieved by an 8-mesh sieve to remove large particles larger than 8 meshes; and sieving the powder by a sieve with 10 meshes to remove small particles smaller than 10 meshes, and finally obtaining the composite powder with the granularity of 8-10 meshes.
Finally, H08A solid welding wire with the diameter phi of 2.5 is used as an electric arc carrier 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 welding bead, and the height and the width of the preset composite powder particle layer are optimally adjusted to obtain the surfacing alloy with the powder filling rate of 0.28.
Before surfacing, the polarity of the automatic welding machine ZD5-1000E is set to be in direct current reverse connection, and surfacing process parameters are shown in Table 1.
And taking the sintered and sieved composite powder particles and the H08A solid welding wire as welding materials, and carrying out submerged-arc welding to fuse the composite powder particle melt and the solid welding wire molten drops into a surfacing molten pool. After the molten pool is air-cooled and solidified to form a first layer of welding line, the surface slag automatically falls off; then, the second layers are separately built up in the same manner. After welding, the surface of the welding seam is smooth and has no defects of cracks, air holes and the like.
TABLE 1 surfacing process parameters of composite powder and solid welding wire
The surfacing test sample is processed by a wire cutting method to prepare a wear-resistant test sample with the thickness of 57mm multiplied by 25.5mm multiplied by 6mm, and the macro hardness of the surface of the wear-resistant test sample 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 the sample for 1000 turns, washing, drying, and weighing the initial weight M 0 Then the test is carried out for 1000 turns, and then the steel plate is cleaned, dried and weighed M 1 And the absolute weight loss of the sample in abrasion delta M = M 0 -M 1 。
The following medium chromium alloy described in relation to the proportion 1 was used as a standard sample, and the relative wear coefficient ∈ = absolute weight loss of standard sample/absolute weight loss of sample, and the test results are shown in table 2.
The texture, phase composition and wear profile of the medium chromium alloy of example 1 are shown in fig. 1, fig. 2 and fig. 5, respectively.
Example 2
Before weighing the components, powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, reduced iron powder and the like are sieved by a 60-mesh sieve, and then aluminum powder is sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 49% of high-carbon ferrochromium, 23% of ferroniobium, 11% of flake graphite, 6% of medium-carbon ferromanganese, 4% of ferrotitanium, 2% of ferrosilicon, 2.5% of aluminum powder and 2.5% of reduced iron powder. .
Weighing powder components such as high-carbon ferrochrome, ferrocolumbium, flake graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, aluminum powder, reduced iron powder and the like according to the composition proportion of the composite powder particles, then putting all the weighed powder components into the same container, and fully stirring to mix uniformly to form mixed powder.
Then, adding 5ml of sodium silicate type water glass with Baume degree of 40 and modulus of 3.0 into the mixed powder each time, continuously stirring during the adding process to enable the water glass to evenly infiltrate into the mixed powder until 22ml of sodium silicate type water glass with volume is finally added into 100g of the mixed powder water glass; then rotating the container at a speed of 4-6 revolutions per second to rotate the wet mixed powder and bond the wet mixed powder into composite powder particles; meanwhile, mashing large particles, slightly vibrating the container up and down, then rotating the container until the particle sizes of most of the composite particles are consistent, and standing for 10 minutes for shaping to obtain approximately spherical composite particles;
and continuously putting the composite powder particles into a sintering furnace, heating to 280 ℃, preserving the heat for 4 hours, and discharging. Then, the sintered composite powder particles are sieved by an 8-mesh sieve to remove large particles larger than 8 meshes; and sieving the powder by a sieve with 10 meshes to remove small particles smaller than 10 meshes, and finally obtaining the composite powder with the granularity of 8-10 meshes.
Finally, H08A solid welding wire with the diameter phi of 2.5 is used as an electric arc carrier on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; and (3) presetting the screened composite powder particles in a weld bead, and optimally adjusting the height and the width of a preset composite powder particle layer to obtain the surfacing alloy with the powder filling rate of 0.30.
The remaining steps and the abrasion resistance test were the same as in example 1.
Example 3
Before weighing the components, powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, reduced iron powder and the like are sieved by a 60-mesh sieve, and then aluminum powder is sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 50% of high-carbon ferrochrome, 25% of ferroniobium, 10% of flake graphite, 4% of medium-carbon ferromanganese, 4% of ferrotitanium, 3% of ferrosilicon, 3% of aluminum powder and 1% of reduced iron powder.
Weighing powder components such as high-carbon ferrochrome, ferrocolumbium, flake graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, aluminum powder, reduced iron powder and the like according to the composition proportion of the composite powder particles, then putting all the weighed powder components into the same container, and fully stirring to mix uniformly to form mixed powder.
Then, 5ml of sodium silicate type water glass with the Baume degree of 36 and the modulus of 3.1 is added into the mixed powder every time, stirring is continuously carried out during the adding process to enable the water glass to be evenly soaked into the mixed powder, and 25ml of sodium silicate type water glass with volume is finally added into 100g of the mixed powder water glass; then rotating the container at a speed of 4-6 revolutions per second to rotate the wet mixed powder and bond the wet mixed powder into composite powder particles; simultaneously mashing large particles, slightly vibrating the container up and down, then rotating the container until the particle sizes of most of the composite particles are consistent, and standing for 10 minutes to shape to obtain approximately spherical composite particles;
and continuously putting the composite powder particles into a sintering furnace, heating to 320 ℃, preserving the heat for 3 hours, and discharging. Then, the sintered composite powder particles are sieved by an 8-mesh sieve to remove large particles larger than 8 meshes; and sieving the powder by a sieve with 10 meshes to remove small particles smaller than 10 meshes, and finally obtaining the composite powder with the granularity of 8-10 meshes.
Finally, H08A solid welding wire with the diameter phi of 2.5 is used as an electric arc carrier on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; and (3) presetting the screened composite powder particles in a weld bead, and optimally adjusting the height and the width of a preset composite powder particle layer to obtain the surfacing alloy with the powder filling rate of 0.27.
The remaining procedures and the abrasion resistance test were the same as in example 1.
Comparative example 1
Before weighing the components, powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, reduced iron powder and the like are sieved by a 60-mesh sieve, and then aluminum powder is sieved by a 300-mesh sieve. The composite powder particles comprise the following powder components in percentage by weight: 48% of high-carbon ferrochromium, 24% of ferroniobium, 6% of flake graphite, 5% of medium-carbon ferromanganese, 5% of ferrotitanium, 3% of ferrosilicon, 2% of aluminum powder and 7% of reduced iron powder.
Weighing powder components such as high-carbon ferrochrome, ferrocolumbium, scale graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon, aluminum powder, reduced iron powder and the like according to the composition proportion of the composite powder particles, then putting all the weighed powder components into the same container, and fully stirring to mix uniformly to form mixed powder.
Then, 5ml of sodium silicate type water glass with the Baume degree of 30 and the modulus of 3.3 is added into the mixed powder every time, stirring is continuously carried out during the adding process to enable the water glass to be evenly soaked into the mixed powder, and the sodium silicate type water glass with the volume of 21ml is finally added into every 100g of the mixed powder water glass; then rotating the container at a speed of 4-6 revolutions per second to rotate the wet mixed powder and bond the wet mixed powder into composite powder particles; meanwhile, mashing large particles, slightly vibrating the container up and down, then rotating the container until the particle sizes of most of the composite particles are consistent, and standing for 10 minutes for shaping to obtain approximately spherical composite particles;
and continuously putting the composite powder particles into a sintering furnace, heating to 290 ℃, preserving heat for 3 hours, and discharging. Then, the sintered composite powder particles are sieved by a sieve with 8 meshes, and large particles larger than 8 meshes are removed; and then sieving the powder by a sieve of 10 meshes to remove small particles smaller than 10 meshes, and finally obtaining the composite powder particles with the particle size of 8-10 meshes.
Finally, H08A solid welding wire with the diameter phi of 2.5 is used as an electric arc carrier on a Q235A steel plate with the length of 160mm, the width of 75mm and the thickness of 16 mm; and (3) presetting the screened composite powder particles in a weld bead, and optimally adjusting the height and the width of a preset composite powder particle layer to obtain the surfacing alloy with the powder filling rate of 0.28.
The surfacing process parameters, polarity setting and surfacing process of the automatic welding machine ZD5-1000E used in the comparative example 1 are the same as those of the example 1. The abrasion resistance test was conducted in the same manner as in example 1.
The structure morphology, phase composition and wear morphology of the medium chromium alloy prepared by the composite powder particle surfacing shown in the comparative example 1 are respectively shown in fig. 3, fig. 4 and fig. 6, and the medium chromium alloy in the comparative example 1 is used as a comparative sample.
TABLE 2 wear resistance of wear resistant particles of medium chromium alloy prepared by bead welding comparative example and example
As can be seen from Table 2, the relative wear coefficient epsilon of the chromium alloy prepared by the composite powder particle surfacing welding of the invention is 1.49-1.69 times that of the surfacing alloy prepared by the composite powder particles with slightly lower carbon content, which shows that the surfacing alloy prepared by the composite powder particles has good wear resistance.
As can be seen from the attached drawings 1 and 2, the surfacing alloy structure prepared by using the composite powder particles and the H08A solid welding wire as welding materials mainly comprises ferrite, (Nb, ti) C, (Fe, cr) 7 C 3 And (Fe, cr) 3 C, and the like.
In addition, as can be seen from the attached FIG. 1, the mesochrome alloy prepared by the method of the present invention contains peritectic crystals (Fe, cr) 7 C 3 The phases are granular and are not in a whole block shape, but are arranged into a net-shaped phase along cellular grain boundaries, the macroscopic hardness of the alloy is 57-59 HRC, no cracks are generated in the preheating-free surfacing welding layer II, and the medium chromium alloy prepared by the powder particles has higher toughness, so that the over-strong rigidity caused by the net-shaped carbide along the whole crystal block is mainly avoided.
The composite particles used in comparative example 1 differed only in flake graphite content from those of example 1, and the other components and the build-up welding process were identical. As can be seen from fig. 3 and 4, the mesochrome alloy cellular phase prepared in comparative example 1 consists of bulk ferrite and a white (Nb, ti) C phase precipitated in situ therein; edgewise carbide (Fe, cr) 7 C 3 The phases are isolated as boron clusters and platelets, and although the rigidity of the clusters along the crystal carbide is very low, the macro hardness of the alloy is only 45.9HRC, which is obviously lower than that of the chromium alloy shown in example 1. As can be seen from the comparison between FIGS. 1 and 3, only the white (Nb, ti) C phase is precipitated in the medium chromium alloy of comparative example 1, which is insufficient for strengthening the second phase of the cellular crystal,the tips of the abrasive particles tend to wedge into the alloy increasing the amount of wear.
Comparing the wear appearance of the two overlay welding alloys shown in the attached figures 5 and 6, under the same wear test condition, the wear surface of the chromium alloy prepared by the composite powder particle overlay welding has less scratches, a plurality of furrows are cut into a particle phase to show stopping signs, the wear is uniform, and the wear mechanism is mainly micro-cutting of abrasive particles. The wear surface of the medium chromium alloy shown in comparative example 1 has more scratches, the scratches are coherent, the spalling pit is larger, the wear mechanism is also micro cutting of abrasive particles, but the wear weight loss is obviously higher than that of the medium chromium alloy prepared by the composite particles, which shows that the medium chromium alloy surfacing welded by the composite particles has better wear resistance, and can be used for surfacing of wear-resistant alloy layers of parts under the wear working condition of the abrasive particles, such as wear-resistant belts of oil drill pipe joints.
Claims (8)
1. Composite powder particles of a wear-resistant belt for overlaying a drill rod joint are prepared into composite powder particles with the particle size of 8-10 meshes by the preparation process steps of weighing and sieving the contained powder components, dry mixing, adding water glass for wet mixing, adhering and granulating, sintering at low temperature and sieving the powder particles;
the composite powder particles comprise the following powder components in percentage by weight: high-carbon ferrochrome with 48-50% of chromium content of 68-72% and carbon content of 8%; 23-25% ferrocolumbium containing 60% niobium; 10-12% of flake graphite with carbon content not less than 98%; 4-6% of medium carbon ferromanganese with manganese content of 78-85% and carbon content of 1.5%; 4-5% of ferrotitanium with titanium content of 25-35%; 2-3% of ferrosilicon with silicon content of 40-47%; 2-3% of aluminum powder with aluminum content not less than 99%; the rest is reduced iron powder with iron content not less than 98%.
2. The composite powder particle of the wear-resistant belt for overlaying the drill rod joint according to claim 1, wherein the composite powder particle comprises the following components in percentage by weight: the powder components of high-carbon ferrochrome, ferroniobium, flake graphite, medium-carbon ferromanganese, ferrotitanium, ferrosilicon and reduced iron powder contained in the composite powder particles are sieved by a sieve of 60 meshes, and the powder components of aluminum powder are sieved by a sieve of 300 meshes and then weighed.
3. The composite powder particle of the wear-resistant belt for overlaying the drill rod joint according to claim 1, wherein the composite powder particle comprises the following components in percentage by weight: the water glass added into the mixed powder is sodium silicate, the Baume degree is 30-40, and the modulus is 3.0-3.3.
4. The composite powder particle of the wear-resistant belt for overlaying the drill rod joint according to claim 1, wherein the composite powder particle comprises the following components in percentage by weight: adding water glass to the mixed powder in a manner of 20-25 ml of sodium silicate type water glass per 100g of the mixed powder, and wet-mixing.
5. The composite powder particle of the wear-resistant belt for overlaying the drill rod joint according to claim 1, wherein the composite powder particle comprises the following components in percentage by weight: sintering the composite powder particles at the low temperature of 250-350 ℃ and keeping the temperature for 2-4 hours, and then discharging the powder particles out of the furnace.
6. A method of applying the composite powder particles of claim 1, wherein: before welding, the composite powder particles are preset in a welding bead, H08A solid welding wire with the diameter phi of 2.5mm is used as an electric arc carrier, and submerged arc surfacing is carried out by adopting a direct-current power supply reversal method, so that the composite powder particle melt and the solid welding wire are molten and fused into a surfacing molten pool, and the (Nb, ti) C-phase reinforced medium chromium alloy with the powder filling rate of 0.27-0.30 and the macroscopic hardness of more than 57HRC is obtained.
7. A method of applying composite powder particles as claimed in claim 6, wherein: the control value of the surfacing current is 410-420A, and the travelling speed of the welding machine trolley is 15-16 m/h.
8. A method of applying composite powder particles as claimed in claim 6, wherein: the welding flux for submerged arc surfacing is a smelting welding flux HJ260.
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