CN108856721B - Preparation process of three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder - Google Patents
Preparation process of three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder Download PDFInfo
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- CN108856721B CN108856721B CN201810789191.2A CN201810789191A CN108856721B CN 108856721 B CN108856721 B CN 108856721B CN 201810789191 A CN201810789191 A CN 201810789191A CN 108856721 B CN108856721 B CN 108856721B
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- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 title claims abstract description 163
- 229910000897 Babbitt (metal) Inorganic materials 0.000 title claims abstract description 113
- 239000000843 powder Substances 0.000 title claims abstract description 104
- 238000010146 3D printing Methods 0.000 title claims abstract description 41
- 239000002131 composite material Substances 0.000 title claims abstract description 34
- 238000002360 preparation method Methods 0.000 title claims abstract description 15
- 239000000463 material Substances 0.000 claims abstract description 55
- 238000004372 laser cladding Methods 0.000 claims abstract description 34
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 32
- 238000000576 coating method Methods 0.000 claims abstract description 23
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 22
- 239000011248 coating agent Substances 0.000 claims abstract description 22
- 239000010959 steel Substances 0.000 claims abstract description 22
- 229910000975 Carbon steel Inorganic materials 0.000 claims abstract description 20
- 239000010962 carbon steel Substances 0.000 claims abstract description 20
- 230000009471 action Effects 0.000 claims abstract description 19
- 229910052751 metal Inorganic materials 0.000 claims abstract description 18
- 239000007788 liquid Substances 0.000 claims abstract description 17
- 239000002184 metal Substances 0.000 claims abstract description 17
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 238000004506 ultrasonic cleaning Methods 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 12
- 244000137852 Petrea volubilis Species 0.000 claims abstract description 9
- 238000005498 polishing Methods 0.000 claims abstract description 9
- 238000003801 milling Methods 0.000 claims abstract description 4
- 238000005507 spraying Methods 0.000 claims abstract description 4
- 238000005119 centrifugation Methods 0.000 claims abstract description 3
- 238000001035 drying Methods 0.000 claims abstract description 3
- 238000005253 cladding Methods 0.000 claims description 40
- 238000000034 method Methods 0.000 claims description 32
- 230000008569 process Effects 0.000 claims description 27
- 238000004321 preservation Methods 0.000 claims description 23
- 239000007789 gas Substances 0.000 claims description 20
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 18
- 230000001681 protective effect Effects 0.000 claims description 16
- 238000004519 manufacturing process Methods 0.000 claims description 11
- 239000002245 particle Substances 0.000 claims description 10
- NNIPDXPTJYIMKW-UHFFFAOYSA-N iron tin Chemical compound [Fe].[Sn] NNIPDXPTJYIMKW-UHFFFAOYSA-N 0.000 claims description 8
- 239000002904 solvent Substances 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 238000007711 solidification Methods 0.000 claims description 4
- 230000008023 solidification Effects 0.000 claims description 4
- 238000012546 transfer Methods 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 229910052787 antimony Inorganic materials 0.000 claims description 3
- 229910052785 arsenic Inorganic materials 0.000 claims description 3
- 229910052797 bismuth Inorganic materials 0.000 claims description 3
- 229910052793 cadmium Inorganic materials 0.000 claims description 3
- 229910052745 lead Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 229910001562 pearlite Inorganic materials 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 238000012545 processing Methods 0.000 claims description 3
- 238000000926 separation method Methods 0.000 claims description 3
- 229910052717 sulfur Inorganic materials 0.000 claims description 3
- 229910000859 α-Fe Inorganic materials 0.000 claims description 3
- 229910045601 alloy Inorganic materials 0.000 abstract description 39
- 239000000956 alloy Substances 0.000 abstract description 39
- 230000008878 coupling Effects 0.000 abstract 1
- 238000010168 coupling process Methods 0.000 abstract 1
- 238000005859 coupling reaction Methods 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 56
- 239000000758 substrate Substances 0.000 description 19
- 238000002844 melting Methods 0.000 description 11
- 230000008018 melting Effects 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 7
- 239000012071 phase Substances 0.000 description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 6
- 238000000861 blow drying Methods 0.000 description 6
- 239000010936 titanium Substances 0.000 description 6
- 229910052719 titanium Inorganic materials 0.000 description 6
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 5
- 239000010949 copper Substances 0.000 description 5
- 229910000765 intermetallic Inorganic materials 0.000 description 5
- 239000002356 single layer Substances 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 229910017091 Fe-Sn Inorganic materials 0.000 description 4
- 229910017142 Fe—Sn Inorganic materials 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000000889 atomisation Methods 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 230000006698 induction Effects 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- 229910018471 Cu6Sn5 Inorganic materials 0.000 description 2
- 229910018320 SbSn Inorganic materials 0.000 description 2
- 238000001856 aerosol method Methods 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000009689 gas atomisation Methods 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000001996 bearing alloy Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000000635 electron micrograph Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000004064 recycling Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000001878 scanning electron micrograph Methods 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 239000012265 solid product Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 230000007480 spreading Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
- C23C24/106—Coating with metal alloys or metal elements only
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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- Mechanical Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Optics & Photonics (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention provides a preparation process of a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder, which comprises the following steps: after high-low temperature circulating embrittlement treatment, the tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and a secondary laminar flow spraying system consisting of a limiting nozzle and a close coupling nozzle is used for spraying high-pressure airflow to atomize and crush the metal liquid into liquid drops, and the liquid drops are separated, cooled and solidified under the action of free fall and centrifugation to obtain tin-based babbit alloy powder; cooling air after the carbon steel is subjected to heat treatment, preheating, immersing into a tin furnace for coating treatment, taking out, polishing by using coarse sand paper, performing ultrasonic cleaning, and drying by using nitrogen to obtain a pretreated base material; conveying tin-based babbit metal powder to the pretreated base material while performing laser cladding, performing multilayer and multi-channel laser cladding on the surface of the steel base material, and finally performing surface and edge milling to form the three-dimensional printing composite material based on the micron-sized tin-based babbit metal powder.
Description
Technical Field
The invention belongs to the technical field of Babbitt metal coatings, and particularly relates to a preparation process of a three-dimensional printing composite material based on micron-sized tin-based Babbitt metal powder.
Background
The tin-based babbit alloy has excellent wear resistance and corrosion resistance, is a main material for manufacturing the fluid lubrication sliding bearing bush, and puts higher requirements on the bearing capacity and reliability of the bearing bush material along with the development of a modern unit to large scale and high speed, and the bearing capacity has a great relationship with the component proportion of the material and the structural design. The metal three-dimensional printing technology is characterized in that metal powder is used as a raw material, special materials such as the metal powder are stacked and bonded layer by layer through a software layering dispersion and numerical control forming system in modes such as laser beams and hot melting nozzles according to a designed three-dimensional model, solid products are processed and manufactured on 3D printing equipment, the metal three-dimensional printing technology is applied to bearing bush materials, more possibilities are provided for structural design of the bearing bush materials, and the performance of the bearing bush materials is developed towards refinement.
The metal three-dimensional printing technology has higher requirements on metal powder, and not only requires that the metal powder has high purity, low oxygen content, good sphericity, fine powder particle size and narrow distribution, but also has good plasticity, fluidity and recycling property. The main metal elements of the metal 3D printing powder commonly used at present are iron, titanium, nickel, aluminum, copper, cobalt, chromium, silver, gold and the like. Chinese patent CN107498059A discloses a method for preparing titanium-based spherical powder with refined particle size by an aerosol method, which comprises the steps of loading a titanium-based raw material and a tin material into a melting crucible, then placing the melting crucible into a melting chamber of vacuum induction melting gas atomization equipment for vacuum induction melting, filling 0-0.8bar of argon gas after the melting is completely melted, enabling the molten liquid to freely fall into an atomization chamber through a heated graphite guide pipe, carrying out vacuum induction melting gas atomization treatment under the argon gas pressure of 10-110bar to obtain atomized powder, and collecting the atomized powder to obtain the titanium-based spherical powder. Tin with the content of 2% is added into the titanium-based spherical powder prepared by the method to reduce the viscosity of molten liquid after smelting, the yield of the powder with the particle size of less than 45 mu m in the titanium-based spherical powder is not less than 28%, the internal pores of the powder are reduced, and the quantity of the hollow powder is reduced. The laser 3D printing manufacturing method of the sink roller shaft sleeve bearing bush disclosed by the Chinese patent CN104525945B comprises the steps of firstly processing a metal substrate to be flat, wiping the metal substrate with acetone to remove oil, then adding one or more of Fe-based, Ni-based or Co-based metal powder and 20-150 mu m mixture powder of W, Mo, carbide or nitride which resists corrosion of molten Zn and Al into a powder feeder, wherein the power of the laser is 1000-5000W; feeding Ar gas or N2 gas according to the powder feeding amount of 5-50 g/min, and feeding the powder into a laser coaxial cladding head; dividing a shaft sleeve bearing bush drawing into a plurality of layers of concentric rings, wherein the layer thickness is 0.2-5 mm, each layer of concentric ring is divided into a plurality of rings, the width is 1-6 mm, the diameter of a laser beam focused by a coaxial cladding head is 1-10 mm, and the moving speed of the cladding head relative to a workpiece is set to be 100-1000 mm/min; adopting lap cladding, controlling the lap ratio to be 20-60%, cladding a plurality of concentric rings, and moving the cladding head upwards by a distance of one ring layer thickness after finishing cladding; cladding is carried out from the substrate, and then cladding work is repeated until the cladding of the whole shaft sleeve bearing bush is completed; and finally, removing the base plate to obtain the bearing bush of the sink roll shaft sleeve. According to the prior art, metal powder with different properties can be prepared to form a three-dimensional alloy structure in a laser cladding mode through a three-dimensional printing technology, but the melting point of the tin-based babbitt alloy is low, the microscopic morphology and properties of the tin-based babbitt alloy can be directly influenced by technological parameters such as temperature in the preparation and use processes, and the service life of the material is further influenced.
Disclosure of Invention
The technical problem to be solved by the invention is to provide a preparation process of a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder, which comprises the steps of firstly carrying out embrittlement treatment on a tin-based babbitt metal ingot, carrying out aerial fog treatment to obtain the tin-based babbitt metal powder with the particle size of less than 45 mu m, then conveying the tin-based babbitt metal powder while carrying out laser cladding, and carrying out multilayer and multi-channel laser cladding on the surface of a pretreated base material to form the three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder. The three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder prepared by the invention has good surface flatness, and the tin-based babbitt metal has fine microstructure and strong bonding force with a base material.
In order to solve the technical problems, the technical scheme of the invention is as follows:
a preparation process of a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder is characterized by comprising the following steps of: the method comprises the following steps:
(1) performing high-low temperature circulating embrittlement treatment on the tin-based Babbitt metal ingot to obtain a pretreated tin-based Babbitt metal ingot;
(2) enabling the pretreated tin-based babbitt metal ingot prepared in the step (1) to flow downwards from a flow guide nozzle, atomizing and crushing metal liquid into liquid drops by using high-pressure airflow sprayed by the nozzle through a secondary laminar flow spraying system consisting of a limiting nozzle and a tightly coupled nozzle, and separating, cooling and solidifying the liquid drops under the actions of free fall and centrifugation to obtain tin-based babbitt metal powder;
(3) after heat treatment, cooling carbon steel by air, preheating, immersing in a tin furnace for coating treatment, taking out, polishing by coarse sand paper, performing ultrasonic cleaning, and drying by nitrogen to obtain a pretreated base material;
(4) and (3) conveying the tin-based babbitt metal powder prepared in the step (1) while carrying out laser cladding on the pretreated base material prepared in the step (3), carrying out multilayer and multi-channel laser cladding on the surface of the steel base material, and finally carrying out surface and edge milling processing to form the micron-sized tin-based babbitt metal powder-based three-dimensional printing composite material.
Preferably, in the step (1), the tin-based babbitt metal ingot comprises the following components in percentage by mass: the balance of Sn, 5.5 to 6.5 percent of Cu, 10.0 to 12.0 percent of Sb, less than or equal to 0.1 percent of Fe, less than or equal to 0.01 percent of Zn, less than or equal to 0.03 percent of Bi, less than or equal to 0.1 percent of As, less than or equal to 0.01 percent of Al, less than or equal to 0.35 percent of Pb, less than or equal to 0.35 percent of Cd, and less than or equal to 0.55 percent.
Preferably, in the step (1), the high-low temperature cyclic embrittlement treatment process includes: the first stage is to keep the tension of 0.3-0.5MPa around the tin-based Babbitt ingot, keep the temperature for 0.5-1h under the environment of minus 20 to minus 60 ℃, and then transfer to the environment of 60-80 ℃ for heat preservation treatment for 2-4h, and the second stage is to keep the tension of 0.1-0.3MPa around the tin-based Babbitt ingot, keep the temperature for 15-30min under the environment of minus 60 to minus 100 ℃, and then transfer to the environment of 100 ℃ to 120 ℃ for heat preservation treatment for 1-3 h.
Preferably, in the step (2), the atomization process includes: under the action of 1000NM 3/h high-pressure airflow with 99.999% purity nitrogen, firstly treating for 5-10min under the conditions of vacuum degree of 4.2-5.6Pa, pressure of 2.0-3.1Mpa and temperature of 800-.
Preferably, in the step (2), the yield of the tin-based babbitt metal powder is more than 90%, the content of the tin-based babbitt metal powder with the particle diameter of less than 45 μm is more than or equal to 50%, and the particle sphericity Ψ 0 of the tin-based babbitt metal powder is more than or equal to 0.95.
Preferably, in the step (2), the rotation speed of the separation, cooling and solidification is 500-.
Preferably, in the step (3), the carbon steel material is a carbon steel material having a ferrite and pearlite structure, and the carbon steel material has a composition of, in weight percent: 0.17-0.24 percent of C, 0.17-0.37 percent of Si, 0.35-0.65 percent of Mn, less than or equal to 0.25 percent of S, less than or equal to 0.035 percent of P, less than or equal to 0.25 percent of Cr, less than or equal to 0.25 percent of Ni, less than or equal to 0.25 percent of Cu, and the balance of Fe, wherein the tensile strength of the carbon steel is more than or equal to 410MPa, the yield strength is more than or equal to 245MPa, and the hardness after heat treatment is.
Preferably, in the step (3), the solvent for ultrasonic cleaning is acetone, the power for ultrasonic cleaning is 50-200W, and the time is 5-10 min.
Preferably, in the step (3), the iron-tin coating with a thickness of 18-20 μm is formed on the surface of the pretreated substrate.
Preferably, in the step (4), the process parameters of the multilayer and multi-pass laser cladding are as follows: the first layer of process parameters: the laser power is 600-2800W, the scanning speed of the laser beam is 18-22mm/s, the powder feeding speed is 15-22g/min, the lap joint rate between the channels is 30-50%, the protective gas flow is 0.3-0.5MPa, the spot size is 3-3.4mm, and the technological parameters of the second layer and the subsequent cladding layer are as follows: the laser power is 600-1200w, the scanning speed of the laser beam is 18-22mm/s, the powder feeding speed is 15-22g/min, the lap joint rate between the channels is 30-50%, the protective gas flow is 0.3-0.5MPa, and the spot size is 3-3.4 mm.
The main raw materials selected by the invention are tin-based babbitt metal powder and a steel substrate, because the tin-based babbitt metal and the steel substrate have larger difference in thermal physical property and cannot be metallurgically bonded, the surface of the steel substrate is subjected to hot dip tinning treatment, the surface of the steel substrate is cleaned, and a high-strength and brittle Fe-Sn intermetallic compound is formed at the bonding interface of the tin-based babbitt metal and the steel substrate, so that the tin-based babbitt metal and the steel substrate achieve the interatomic connection required by laser cladding, but the toughness of a joint is reduced due to the excessively high content of the Fe-Sn intermetallic compound, and the bonding performance is reduced on the contrary, therefore, the thickness of the Fe-Sn intermetallic compound is controlled to be 18-20 mu m, the connection requirement is met, and the mechanical property of a product is not influenced.
The first layer of cladding is mainly the combination of the tin-based babbit alloy and the steel substrate of the Fe-Sn intermetallic compound layer, the combination quality of the tin-based babbit alloy and the substrate is directly influenced by the quality of the combination, because the subsequent cladding layers are all cladded on the tin-based babbit alloy substrate, the liquid phase point temperature of the tin-based babbit alloy is 370 ℃, the temperature is low and belongs to low-melting point alloy, if the input energy is large, the molten pool spreading is caused to be open in the cladding process, even the molten pool collapse is caused to cause the liquid flow of the tin-based babbit alloy, so the liquid phase point temperature based on the tin-based babbit alloy is 370 ℃, the melting point of the steel substrate is 1530 ℃, and the technological parameters of single-channel and multi-channel are different.
Researches find that when a substrate is used as a material to perform laser cladding on a tin-based babbitt metal cladding layer, in a process for preparing a tin-based babbitt metal bottom layer by multiple layers in a single process, the laser power must be more than 1400w to ensure that the tin-based babbitt metal cladding layer and the substrate form good combination; but the laser power cannot be too large, when the laser power is larger than or equal to 2600W, the surface of the tin-based babbit alloy cladding layer has obvious oxidation blackening phenomenon, when the laser power is 1400-2600W, the surface of the cladding layer is smooth and plump, the cladding process is relatively stable, no obvious splashing phenomenon exists, and the tin-based babbit alloy bottom layer is formed. The upper surface of a single-layer single-channel cladding layer is regarded as a circular arc in the laser cladding process, the lapping between channels needs to keep the surface smoothness, and the area of the overlapped part is equal to the area of the vacant part at the top of the cladding layer. According to the previous cladding experience, the lapping rate between the tracks is 40% in order to obtain the cladding layer surface with better surface flatness according to the lapping rate between the cladding layer tracks which is (W-C)/W. And calculating the lane-to-lane deviation distance C according to a lap joint ratio calculation formula eta (W-C)/W and the size parameter of the single-layer single-lane tin-based babbitt metal cladding layer obtained by corresponding process parameters in the process of cladding the first layer and the subsequent cladding layer.
Compared with the prior art, the invention has the following beneficial effects:
(1) the main raw material of the three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder is the micron-sized tin-based babbitt metal powder, the micron-sized tin-based babbitt metal powder is a tin-based babbitt metal ingot subjected to high-low temperature circulating embrittlement treatment, and the pretreated tin-based babbitt metal ingot is small in binding force, large in brittleness and small in toughness, so that the tin-based babbitt metal ingot is more favorable for later aerial fog atomization and balling, the particle size of the tin-based babbitt metal powder is reduced, the sphericity is improved, the requirements of a 3D printing technology on the metal powder are fully met, the technical difficulty of laser cladding is reduced, and the structural precision of the three-dimensional printing composite material of the micron-. The invention combines the aerosol method and the laser cladding technology, and the prepared three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder has good surface smoothness, fine tin-based babbitt metal microstructure and strong bonding force with a base material.
(2) The three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder, prepared by the method, can be directly used as a part, also can be used in combination with other parts, also can be used as a modified coating attached to the surface of a collector, has strong structure variability and wide application range, and has good market competitiveness in the preparation of parts such as a bearing bush, a sliding bearing and the like.
Drawings
The accompanying drawings, which are included to provide a further understanding of the invention and are incorporated in and constitute a part of this application, illustrate embodiment(s) of the invention and together with the description serve to explain the principles of the invention:
FIG. 1 is a scanning electron micrograph of a tin-based babbitt metal powder.
FIG. 2 is a morphology chart of a single layer tin-based babbitt metal coating material under different laser powers.
FIG. 2 is a graph showing the morphology of a single-layer single-channel tin-based Babbitt metal cladding layer under the conditions of laser power of 600-2800W, laser beam scanning rate of 20mm/s, powder feeding rate of 19.79g/min and spot size of 3.22mm, and it can be known that a single-layer single-channel tin-based Babbitt metal cladding layer with a good morphology is selected between 1400W-2600W, that is, when the laser power is 2000W, the surface of the obtained cladding layer is smooth, the appearance of the cladding layer is plump, and the surface has no obvious oxidation phenomenon.
Figure 3 is a topographical view of a three-dimensional printed composite material based on micron-sized tin-based babbitt metal powder.
As can be seen from the attached figure 3, the forming surface of the three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder is relatively flat and smooth, the molten pool collapse caused by energy accumulation also exists on one side perpendicular to the scanning speed direction, and the tin-based babbitt metal cladding layer flows outwards.
FIG. 4 is an electron microscope image of the interface boundary between the tin-based Babbitt alloy coating layer and the steel material in the three-dimensional printing composite material based on the micron-sized tin-based Babbitt alloy powder.
In the attached figure 4, an obvious white and bright intermediate interface layer is arranged between the steel base material and the tin-based babbit alloy cladding layer, and the generation of the intermediate interface layer shows that the tin-based babbit alloy and the steel base material realize better metallurgical bonding, which is important for improving the bonding strength between the two alloys.
Fig. 5 is an electron micrograph of a tin-based babbitt coating based on 3D printing technology.
As shown in the attached figure 5, more diamond-shaped and star-shaped blocky precipitates are precipitated in the microstructure of the tin-based babbitt alloy, wherein the blocky precipitates are mainly SbSn phases, and more white and bright fine needle-shaped tissues are dispersed in a black matrix phase, wherein the fine needle-shaped tissues are Cu6Sn5 phases. The SbSn and Cu6Sn5 intermetallic compounds are precipitated in the solidification process of a molten pool and are relatively uniformly distributed in the matrix phase, so that on one hand, the wear resistance and hardness of the matrix phase are increased, and on the other hand, when the bearing alloy rubs and wears, the matrix phase is supported, and the relatively fast wear of the relatively soft tin-based solid solution phase is prevented.
FIG. 6 is a graph of EDS line scans of a tin-based babbitt coating and a steel substrate surface.
As can be seen from the EDS line scan of figure 6, elements from a steel substrate to a tin-based babbitt metal bottom layer are in linear transition, an obvious transition layer is formed between the two metals, and the generation of the transition layer plays an important role in improving the bonding strength between the two alloys.
Detailed Description
The present invention will be described in detail with reference to specific embodiments, which are illustrative of the invention and are not to be construed as limiting the invention.
The tin-based Babbitt metal ingot comprises the following components in percentage by mass: the balance of Sn, 5.5 to 6.5 percent of Cu, 10.0 to 12.0 percent of Sb, less than or equal to 0.1 percent of Fe, less than or equal to 0.01 percent of Zn, less than or equal to 0.03 percent of Bi, less than or equal to 0.1 percent of As, less than or equal to 0.01 percent of Al, less than or equal to 0.35 percent of Pb, less than or equal to 0.35 percent of Cd, and less than or equal to 0.55 percent.
The base material is carbon steel with a structure of ferrite and pearlite, and the carbon steel comprises the following components in percentage by weight: 0.17-0.24 percent of C, 0.17-0.37 percent of Si, 0.35-0.65 percent of Mn, less than or equal to 0.25 percent of S, less than or equal to 0.035 percent of P, less than or equal to 0.25 percent of Cr, less than or equal to 0.25 percent of Ni, less than or equal to 0.25 percent of Cu, and the balance of Fe, wherein the tensile strength of the carbon steel is more than or equal to 410MPa, the yield strength is more than or equal to 245MPa, and the hardness after heat treatment is.
Example 1:
(1) performing high-low temperature circulating embrittlement treatment on a tin-based Babbitt metal ingot, wherein in the first stage, a tensile force of 0.3MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 0.5h in an environment of 20 ℃ below zero and is transferred to an environment of 60 ℃ for heat preservation treatment for 2h, and in the second stage, a tensile force of 0.1MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 15min in an environment of 60 ℃ below zero and is transferred to an environment of 100.
(2) The pretreated tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and is treated for 5min under the action of 1000NM 3/h high-pressure airflow with 99.999% nitrogen purity at the vacuum degree of 4.2Pa, the pressure of 2.0MPa and the temperature of 800 ℃ under the action of 1000NM 3/h high-pressure airflow, then is treated for 30min under the conditions of the vacuum degree of 3.5Pa, the pressure of 3.4MPa and the temperature of 1050 ℃, and finally is treated for 45min under the conditions of the vacuum degree of 3.0Pa, the pressure of 5.5MPa and the temperature of 1450 ℃, liquid drops are separated, cooled and solidified for 5min under the centrifugal action of free fall and the rotating speed of 500r/min, and the tin-based babbit alloy powder is obtained.
(3) The preparation method comprises the following steps of carrying out heat treatment on carbon steel at 900 ℃, carrying out air cooling, preheating to 170 ℃, immersing in a tin furnace for coating treatment, taking out, polishing with coarse sand paper, carrying out ultrasonic cleaning for 5min at 50W power by using acetone as a solvent, carrying out nitrogen blow-drying, and thus obtaining a pretreated base material, wherein an iron-tin coating with the thickness of 18 microns is formed on the surface of the pretreated base material.
(4) Conveying tin-based babbit alloy powder to the pretreated base material while carrying out laser cladding, and carrying out multilayer and multichannel laser cladding on the surface of the steel base material, wherein the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 2800W, the laser beam scanning rate is 18mm/s, the powder feeding rate is 22g/min, the inter-channel lap joint rate is 30%, the protective gas flow is 0.5MPa, the spot size is 3mm, and the technological parameters of a second layer and a subsequent cladding layer are as follows: the laser power is 600w, the scanning speed of the laser beam is 22mm/s, the powder feeding speed is 15g/min, the lap joint rate between channels is 50%, the protective gas flow is 0.3MPa, the spot size is 3.4mm, and finally, the surface and the edge are milled to form the three-dimensional printing composite material based on the micron-sized tin-based Babbitt alloy powder.
Example 2:
(1) performing high-low temperature circulating embrittlement treatment on a tin-based Babbitt metal ingot, wherein in the first stage, a tensile force of 0.5MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 1h at the temperature of minus 60 ℃, and is transferred to the environment of 80 ℃ for heat preservation treatment for 4h, and in the second stage, a tensile force of 0.3MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 30min at the temperature of minus 100 ℃, and is transferred to the environment of 120 ℃ for.
(2) The pretreated tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and is treated for 10min under the action of 1000NM 3/h high-pressure airflow with 99.999% nitrogen purity, the vacuum degree of 5.6Pa, the pressure of 3.1MPa and the temperature of 1000 ℃ for 10min, then the vacuum degree of 4.0Pa, the pressure of 5.5MPa and the temperature of 1450 ℃ for 60min, finally the vacuum degree of 3.4Pa, the pressure of 6MPa and the temperature of 1600 ℃ for 90min, and liquid drops are separated, cooled and solidified for 40min under the centrifugal action of free fall and the rotating speed of 2000r/min to obtain the tin-based babbit alloy powder.
(3) The preparation method comprises the following steps of carrying out heat treatment on carbon steel at 950 ℃, carrying out air cooling, preheating to 200 ℃, immersing in a tin furnace for coating treatment, taking out, polishing with coarse sand paper, carrying out ultrasonic cleaning for 10min at 200W power by using acetone as a solvent, carrying out nitrogen blow-drying, and thus obtaining a pretreated base material, wherein an iron-tin coating with the thickness of 20 microns is formed on the surface of the pretreated base material.
(4) Conveying tin-based babbit alloy powder to the pretreated base material while carrying out laser cladding, and carrying out multilayer and multichannel laser cladding on the surface of the steel base material, wherein the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 1600W, the laser beam scanning speed is 19mm/s, the powder feeding speed is 20g/min, the lap joint rate between the channels is 35%, the protective gas flow is 0.35MPa, the spot size is 3.3mm, and the technological parameters of a second layer and a subsequent cladding layer are as follows: the laser power is 1000w, the scanning speed of a laser beam is 19.6mm/s, the powder feeding speed is 8g/min, the inter-channel lap joint rate is 35%, the protective gas flow is 0.35MPa, the spot size is 3.3mm, and finally, the surface and the edge are milled to form the three-dimensional printing composite material based on the micron-sized tin-based babbit alloy powder.
Example 3:
(1) performing high-low temperature circulating embrittlement treatment on a tin-based Babbitt metal ingot, wherein in the first stage, a tensile force of 0.4MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 1h at the temperature of minus 40 ℃, and is transferred to the environment of 70 ℃ for heat preservation treatment for 3h, and in the second stage, a tensile force of 0.2MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 20min at the temperature of minus 80 ℃, and is transferred to the environment of 110 ℃ for.
(2) The pretreated tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and is treated for 6min under the action of 1000NM 3/h high-pressure airflow with 99.999% nitrogen purity, wherein the high-pressure airflow is at 4.8Pa under the vacuum degree, 2.6MPa under the pressure and 850 ℃ for 6min, then is treated for 45min under the vacuum degree, 3.8Pa under the pressure, 4.3MPa under the temperature of 1250 ℃, and finally is treated for 60min under the vacuum degree, 3.1Pa under the pressure, 5.8MPa and 1550 ℃ for 10min, and the liquid drops are separated, cooled and solidified under the centrifugal action of free fall and the rotating speed of 1500r/min to obtain the tin-based babbit alloy powder.
(3) The preparation method comprises the following steps of carrying out heat treatment on carbon steel at 910 ℃, carrying out air cooling, preheating to 180 ℃, immersing in a tin furnace for coating treatment, taking out, polishing with coarse sand paper, carrying out ultrasonic cleaning for 7min at 150W power by using acetone as a solvent, carrying out nitrogen blow-drying, and obtaining a pretreated base material, wherein an iron-tin coating with the thickness of 19 mu m is formed on the surface of the pretreated base material.
(4) Conveying tin-based babbit alloy powder to the pretreated base material while carrying out laser cladding, and carrying out multilayer and multichannel laser cladding on the surface of the steel base material, wherein the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 2400W, the laser beam scanning speed is 20.5mm/s, the powder feeding speed is 18.5g/min, the inter-track lap joint rate is 45%, the protective gas flow is 0.45MPa, the spot size is 3.2mm, and the technological parameters of a second layer and a subsequent cladding layer are as follows: the laser power is 800w, the scanning speed of the laser beam is 20mm/s, the powder feeding speed is 19g/min, the lap joint rate between channels is 45%, the protective gas flow is 0.35MPa, the spot size is 3.3mm, and finally, the surface and the edge are milled to form the three-dimensional printing composite material based on the micron-sized tin-based Babbitt alloy powder.
Example 4:
(1) performing high-low temperature circulating embrittlement treatment on a tin-based Babbitt metal ingot, wherein in the first stage, a tensile force of 0.4MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 0.5h at the temperature of minus 45 ℃, and is subjected to heat preservation treatment for 3.5h at the temperature of 75 ℃, and in the second stage, a tensile force of 0.2MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 25min at the temperature of minus 90 ℃, and is subjected to heat preservation treatment for 1.5h at.
(2) The pretreated tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and is treated for 7min under the action of 1000NM 3/h high-pressure airflow with 99.999% nitrogen purity at the vacuum degree of 4.8Pa, the pressure of 2.7MPa and the temperature of 900 ℃ under the action of 1000NM 3/h high-pressure airflow, then is treated for 50min under the conditions of the vacuum degree of 3.8Pa, the pressure of 4.5MPa and the temperature of 1300 ℃, and finally is treated for 75min under the conditions of the vacuum degree of 3.3Pa, the pressure of 5.8MPa and the temperature of 1550 ℃, liquid drops are separated, cooled and solidified for 30min under the centrifugal action of free fall and the rotating speed of 1400r/min, and the tin-based babbit alloy powder is obtained.
(3) The preparation method comprises the following steps of carrying out heat treatment on carbon steel at 940 ℃, carrying out air cooling, preheating to 195 ℃, immersing in a tin furnace for coating treatment, taking out, polishing with coarse sand paper, carrying out ultrasonic cleaning for 7min at 150W power by using acetone as a solvent, carrying out blow-drying with nitrogen, and thus obtaining a pretreated base material, wherein an iron-tin coating with the thickness of 19.5 microns is formed on the surface of the pretreated base material.
(4) Conveying tin-based babbit alloy powder to the pretreated base material while carrying out laser cladding, and carrying out multilayer and multichannel laser cladding on the surface of the steel base material, wherein the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 2500W, the scanning speed of the laser beam is 20.5mm/s, the powder feeding speed is 18g/min, the lap joint rate between the channels is 45%, the flow rate of protective gas is 0.45MPa, the spot size is 3.4mm, and the technological parameters of a second layer and a subsequent cladding layer are as follows: the laser power is 800w, the scanning speed of a laser beam is 21.5mm/s, the powder feeding speed is 19.5g/min, the lap joint rate between channels is 45%, the protective gas flow is 0.35MPa, the spot size is 3.2mm, and finally, the surface and the edge are milled to form the three-dimensional printing composite material based on the micron-sized tin-based babbit alloy powder.
Example 5:
(1) performing high-low temperature circulating embrittlement treatment on a tin-based Babbitt metal ingot, wherein in the first stage, a tensile force of 0.3MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 0.5h in an environment of 60 ℃ below zero and is transferred to an environment of 80 ℃ for heat preservation treatment for 2h, and in the second stage, a tensile force of 0.3MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 30min in an environment of 60 ℃ below zero and is transferred to an environment of 100.
(2) The pretreated tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and is treated for 10min under the action of 1000NM 3/h high-pressure airflow with 99.999% nitrogen purity, wherein the high-pressure airflow is at 4.2Pa under the vacuum degree, 3.1MPa under the pressure and 800 ℃ for 10min, then is treated for 60min under the vacuum degree, 3.5Pa under the pressure of 5.5MPa and 1050 ℃ for 1450 ℃, and finally is treated for 90min under the vacuum degree, 6MPa under the vacuum degree, 3.0Pa under the pressure and 1450 ℃ for separation, cooling and solidification for 40min under the centrifugal action of free fall and 500r/min rotation speed, so that the tin-based babbit alloy powder is obtained.
(3) The preparation method comprises the following steps of carrying out heat treatment on carbon steel at 900 ℃, carrying out air cooling, preheating to 200 ℃, immersing in a tin furnace for coating treatment, taking out, polishing with coarse sand paper, carrying out ultrasonic cleaning for 10min at 50W power by using acetone as a solvent, carrying out nitrogen blow-drying, and thus obtaining a pretreated base material, wherein an iron-tin coating with the thickness of 18 microns is formed on the surface of the pretreated base material.
(4) Conveying tin-based babbit alloy powder to the pretreated base material while carrying out laser cladding, and carrying out multilayer and multichannel laser cladding on the surface of the steel base material, wherein the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 2000W, the laser beam scanning speed is 21.5mm/s, the powder feeding speed is 16g/min, the lap joint rate between the channels is 40%, the protective gas flow is 0.45MPa, the spot size is 3.25mm, and the technological parameters of a second layer and a subsequent cladding layer are as follows: the laser power is 600-1200w, the scanning speed of the laser beam is 19mm/s, the powder feeding speed is 21g/min, the lap joint rate between channels is 30%, the protective gas flow is 0.5MPa, the spot size is 3.4mm, and finally, the three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder is formed by milling the surface and the edge.
Example 6:
(1) performing high-low temperature circulating embrittlement treatment on a tin-based Babbitt metal ingot, wherein in the first stage, a tensile force of 0.5MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 1h at the temperature of minus 20 ℃, and is transferred to the environment of 60 ℃ for heat preservation treatment for 4h, and in the second stage, a tensile force of 0.1MPa is kept on the periphery of the tin-based Babbitt metal ingot, the tin-based Babbitt metal ingot is subjected to heat preservation for 15min at the temperature of minus 100 ℃, and is transferred to the environment of 120 ℃ for.
(2) The pretreated tin-based babbit alloy ingot flows downwards from a flow guide nozzle, and is treated for 5min under the action of 1000NM 3/h high-pressure airflow with 99.999% nitrogen purity at 5.6Pa, 2.0MPa and 1000 ℃ for 5min under the action of 1000NM 3/h high-pressure airflow, then is treated for 30min under the conditions of 4.0Pa, 3.4MPa and 1450 ℃ and finally is treated for 45min under the conditions of 3.4Pa, 5.5MPa and 1600 ℃ and liquid drops are separated, cooled and solidified for 5min under the centrifugal action of free fall and 2000r/min of rotating speed to obtain the tin-based babbit alloy powder.
(3) The preparation method comprises the following steps of carrying out heat treatment on carbon steel at 950 ℃, carrying out air cooling, preheating to 170 ℃, immersing in a tin furnace for coating treatment, taking out, polishing with coarse sand paper, carrying out ultrasonic cleaning for 5min at 200W power by using acetone as a solvent, carrying out nitrogen blow-drying, and thus obtaining a pretreated base material, wherein an iron-tin coating with the thickness of 20 microns is formed on the surface of the pretreated base material.
(4) Conveying tin-based babbit alloy powder to the pretreated base material while carrying out laser cladding, and carrying out multilayer and multichannel laser cladding on the surface of the steel base material, wherein the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 1600W, the laser beam scanning speed is 22mm/s, the powder feeding speed is 15g/min, the lap joint rate between the channels is 50%, the protective gas flow is 0.3MPa, the spot size is 3.4mm, and the technological parameters of a second layer and a subsequent cladding layer are as follows: the laser power is 1200w, the scanning speed of the laser beam is 18mm/s, the powder feeding speed is 22g/min, the lap joint rate between channels is 30%, the protective gas flow is 0.5MPa, the spot size is 3mm, and finally, the surface and the edge are milled to form the three-dimensional printing composite material based on the micron-sized tin-based babbitt metal powder.
The results of yield, average particle size and sphericity of the tin-based babbitt alloy powders prepared in examples 1-6 are set forth in the following table:
the bonding strength of the tin-based babbitt alloy coating to the substrate in the three-dimensional printed composite prepared in example 1, with different alloy layer thicknesses based on micron-sized tin-based babbitt alloy powder, is shown in the following table:
| thickness of alloy layer/mm | Maximum shear force Fmax/KN | Bonding strength, σ ch/Mpa |
| 5 | 22.489 | 104.895 |
| 8 | 28.194 | 140.360 |
The foregoing embodiments are merely illustrative of the principles and utilities of the present invention and are not intended to limit the invention. Any person skilled in the art can modify or change the above-mentioned embodiments without departing from the spirit and scope of the present invention. Accordingly, it is intended that all equivalent modifications or changes which can be made by those skilled in the art without departing from the spirit and technical spirit of the present invention be covered by the claims of the present invention.
Claims (9)
1. A preparation process of a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder is characterized by comprising the following steps of: the method comprises the following steps:
(1) performing high-low temperature circulating embrittlement treatment on the tin-based Babbitt metal ingot to obtain a pretreated tin-based Babbitt metal ingot;
(2) enabling the pretreated tin-based babbitt metal ingot prepared in the step (1) to flow downwards from a flow guide nozzle, atomizing and crushing metal liquid into liquid drops by using high-pressure airflow sprayed by the nozzle through a secondary laminar flow spraying system consisting of a limiting nozzle and a tightly coupled nozzle, and separating, cooling and solidifying the liquid drops under the actions of free fall and centrifugation to obtain tin-based babbitt metal powder;
(3) after heat treatment, cooling carbon steel by air, preheating, immersing in a tin furnace for coating treatment, taking out, polishing by coarse sand paper, performing ultrasonic cleaning, and drying by nitrogen to obtain a pretreated base material;
(4) and (3) conveying the tin-based babbitt metal powder prepared in the step (1) while carrying out laser cladding on the pretreated base material prepared in the step (3), carrying out multilayer and multi-channel laser cladding on the surface of the steel base material, and finally carrying out surface and edge milling processing to form the micron-sized tin-based babbitt metal powder-based three-dimensional printing composite material.
2. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (1), the tin-based Babbitt alloy ingot comprises the following components in percentage by mass: the balance of Sn, 5.5 to 6.5 percent of Cu, 10.0 to 12.0 percent of Sb, less than or equal to 0.1 percent of Fe, less than or equal to 0.01 percent of Zn, less than or equal to 0.03 percent of Bi, less than or equal to 0.1 percent of As, less than or equal to 0.01 percent of Al, less than or equal to 0.35 percent of Pb, less than or equal to 0.35 percent of Cd, and less than or equal to 0.55 percent.
3. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (1), the process of high-low temperature circulating embrittlement treatment comprises the following steps: the first stage is to keep the tension of 0.3-0.5MPa around the tin-based Babbitt ingot, keep the temperature for 0.5-1h under the environment of minus 20 to minus 60 ℃, and then transfer to the environment of 60-80 ℃ for heat preservation treatment for 2-4h, and the second stage is to keep the tension of 0.1-0.3MPa around the tin-based Babbitt ingot, keep the temperature for 15-30min under the environment of minus 60 to minus 100 ℃, and then transfer to the environment of 100 ℃ to 120 ℃ for heat preservation treatment for 1-3 h.
4. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (2), the yield of the tin-based babbitt metal powder is more than 90%, the content of the tin-based babbitt metal powder with the particle size of less than 45 mu m is more than or equal to 50%, and the particle sphericity psi 0 of the tin-based babbitt metal powder is more than or equal to 0.95.
5. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (2), the rotating speed of the separation, cooling and solidification is 500-.
6. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (3), the carbon steel is carbon steel with a structure of ferrite and pearlite, and the carbon steel comprises the following components in percentage by weight: 0.17-0.24 percent of C, 0.17-0.37 percent of Si, 0.35-0.65 percent of Mn, less than or equal to 0.25 percent of S, less than or equal to 0.035 percent of P, less than or equal to 0.25 percent of Cr, less than or equal to 0.25 percent of Ni, less than or equal to 0.25 percent of Cu, and the balance of Fe, wherein the tensile strength of the carbon steel is more than or equal to 410MPa, the yield strength is more than or equal to 245MPa, and the hardness after heat treatment is.
7. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (3), the solvent for ultrasonic cleaning is acetone, the power of ultrasonic cleaning is 50-200W, and the time is 5-10 min.
8. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (3), an iron-tin coating with the thickness of 18-20 μm is formed on the surface of the pretreated base material.
9. The process for preparing a three-dimensional printing composite material based on micron-sized tin-based babbitt metal powder according to claim 1, wherein: in the step (4), the process parameters of the multilayer and multichannel laser cladding are as follows: the first layer of process parameters: the laser power is 600-2800W, the scanning speed of the laser beam is 18-22mm/s, the powder feeding speed is 15-22g/min, the lap joint rate between the channels is 30-50%, the protective gas flow is 0.3-0.5MPa, the spot size is 3-3.4mm, and the technological parameters of the second layer and the subsequent cladding layer are as follows: the laser power is 600-1200w, the scanning speed of the laser beam is 18-22mm/s, the powder feeding speed is 15-22g/min, the lap joint rate between the channels is 30-50%, the protective gas flow is 0.3-0.5MPa, and the spot size is 3-3.4 mm.
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| CN113235087A (en) * | 2021-05-31 | 2021-08-10 | 芜湖舍达激光科技有限公司 | Process for zinc pot roller shaft sleeve surface laser cladding |
| CN113862660B (en) * | 2021-09-10 | 2023-11-14 | 江阴市东泰管件有限公司 | High-compression-resistance butt-welded elbow and processing technology thereof |
| CN115747785B (en) * | 2022-12-07 | 2024-10-29 | 长沙大科激光科技有限公司 | Laser-cold spraying composite remote high-speed laser cladding method |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3985408A (en) * | 1975-10-10 | 1976-10-12 | General Motors Corporation | Bearing having iron sulfur matrix |
| RU2006102741A (en) * | 2006-01-31 | 2007-08-10 | Владилен Борисович Бирюков (RU) | METHOD FOR MODIFICATION OF BABBIT ALLOYS |
| CN102248320A (en) * | 2011-07-06 | 2011-11-23 | 东南大学 | Stannum-based composite babbit metal and method for preparing welding wire |
| CN107803501A (en) * | 2017-11-18 | 2018-03-16 | 北京科技大学 | A kind of laser gain material manufacture method of tin-base babbit component |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103817413B (en) * | 2014-03-20 | 2016-02-17 | 哈尔滨工业大学 | A kind of preparation method of copper-based alloy bearing bush wearing layer |
| CN107936459B (en) * | 2017-12-07 | 2019-08-20 | 中国科学院福建物质结构研究所 | It is a kind of for the composition of fused glass pellet 3D printer, preparation and its application |
-
2018
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3985408A (en) * | 1975-10-10 | 1976-10-12 | General Motors Corporation | Bearing having iron sulfur matrix |
| RU2006102741A (en) * | 2006-01-31 | 2007-08-10 | Владилен Борисович Бирюков (RU) | METHOD FOR MODIFICATION OF BABBIT ALLOYS |
| CN102248320A (en) * | 2011-07-06 | 2011-11-23 | 东南大学 | Stannum-based composite babbit metal and method for preparing welding wire |
| CN107803501A (en) * | 2017-11-18 | 2018-03-16 | 北京科技大学 | A kind of laser gain material manufacture method of tin-base babbit component |
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