CN104589726B - Multiphase dual-scale structural aluminum-tin based composite bearing bush strip and preparation method thereof - Google Patents
Multiphase dual-scale structural aluminum-tin based composite bearing bush strip and preparation method thereof Download PDFInfo
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- CN104589726B CN104589726B CN201410714427.8A CN201410714427A CN104589726B CN 104589726 B CN104589726 B CN 104589726B CN 201410714427 A CN201410714427 A CN 201410714427A CN 104589726 B CN104589726 B CN 104589726B
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- 238000002360 preparation method Methods 0.000 title claims abstract description 31
- 239000002131 composite material Substances 0.000 title claims abstract description 26
- YVIMHTIMVIIXBQ-UHFFFAOYSA-N [SnH3][Al] Chemical compound [SnH3][Al] YVIMHTIMVIIXBQ-UHFFFAOYSA-N 0.000 title abstract description 9
- 239000000843 powder Substances 0.000 claims abstract description 103
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 90
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 89
- 238000000034 method Methods 0.000 claims abstract description 61
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 55
- 239000000956 alloy Substances 0.000 claims abstract description 55
- 238000005096 rolling process Methods 0.000 claims abstract description 38
- 230000008569 process Effects 0.000 claims abstract description 29
- 238000000137 annealing Methods 0.000 claims abstract description 28
- 239000011812 mixed powder Substances 0.000 claims abstract description 28
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 27
- 239000010959 steel Substances 0.000 claims abstract description 27
- 238000005245 sintering Methods 0.000 claims abstract description 23
- 238000005551 mechanical alloying Methods 0.000 claims abstract description 16
- 229910001209 Low-carbon steel Inorganic materials 0.000 claims abstract description 14
- 230000007704 transition Effects 0.000 claims abstract description 9
- 238000005097 cold rolling Methods 0.000 claims abstract description 8
- 238000004381 surface treatment Methods 0.000 claims abstract description 4
- 241000357293 Leptobrama muelleri Species 0.000 claims description 84
- 239000004411 aluminium Substances 0.000 claims description 77
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 40
- 238000000498 ball milling Methods 0.000 claims description 27
- 229910052786 argon Inorganic materials 0.000 claims description 20
- 239000007789 gas Substances 0.000 claims description 20
- 239000000463 material Substances 0.000 claims description 19
- 229910052799 carbon Inorganic materials 0.000 claims description 13
- 229910001128 Sn alloy Inorganic materials 0.000 claims description 11
- 238000001816 cooling Methods 0.000 claims description 10
- 238000007751 thermal spraying Methods 0.000 claims description 10
- 238000001291 vacuum drying Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 9
- 229910000676 Si alloy Inorganic materials 0.000 claims description 8
- 238000005516 engineering process Methods 0.000 claims description 8
- 238000002156 mixing Methods 0.000 claims description 5
- 239000004576 sand Substances 0.000 claims description 5
- 238000005507 spraying Methods 0.000 claims description 5
- 239000000470 constituent Substances 0.000 claims description 4
- 238000010285 flame spraying Methods 0.000 claims description 4
- 238000005498 polishing Methods 0.000 claims description 4
- 230000000750 progressive effect Effects 0.000 claims description 4
- 238000010276 construction Methods 0.000 claims description 3
- 238000009413 insulation Methods 0.000 claims description 3
- 229910001339 C alloy Inorganic materials 0.000 claims description 2
- 238000005488 sandblasting Methods 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 4
- 239000001996 bearing alloy Substances 0.000 abstract description 3
- 239000002159 nanocrystal Substances 0.000 abstract 2
- 229910019086 Mg-Cu Inorganic materials 0.000 abstract 1
- 229910008813 Sn—Si Inorganic materials 0.000 abstract 1
- 239000013078 crystal Substances 0.000 abstract 1
- 235000013619 trace mineral Nutrition 0.000 abstract 1
- 239000011573 trace mineral Substances 0.000 abstract 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 15
- 238000000227 grinding Methods 0.000 description 13
- 239000012071 phase Substances 0.000 description 11
- 238000005266 casting Methods 0.000 description 8
- 239000011521 glass Substances 0.000 description 8
- 230000005496 eutectics Effects 0.000 description 6
- 235000013312 flour Nutrition 0.000 description 6
- 239000000377 silicon dioxide Substances 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 239000011863 silicon-based powder Substances 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005422 blasting Methods 0.000 description 3
- 238000006243 chemical reaction Methods 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 3
- 229910052737 gold Inorganic materials 0.000 description 3
- 239000010931 gold Substances 0.000 description 3
- 230000005484 gravity Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000000758 substrate Substances 0.000 description 3
- RZVAJINKPMORJF-UHFFFAOYSA-N Acetaminophen Chemical compound CC(=O)NC1=CC=C(O)C=C1 RZVAJINKPMORJF-UHFFFAOYSA-N 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910000897 Babbitt (metal) Inorganic materials 0.000 description 2
- 229910000906 Bronze Inorganic materials 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 2
- 240000007594 Oryza sativa Species 0.000 description 2
- 235000007164 Oryza sativa Nutrition 0.000 description 2
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 2
- WIKSRXFQIZQFEH-UHFFFAOYSA-N [Cu].[Pb] Chemical compound [Cu].[Pb] WIKSRXFQIZQFEH-UHFFFAOYSA-N 0.000 description 2
- 239000010974 bronze Substances 0.000 description 2
- 239000000356 contaminant Substances 0.000 description 2
- WCCJDBZJUYKDBF-UHFFFAOYSA-N copper silicon Chemical compound [Si].[Cu] WCCJDBZJUYKDBF-UHFFFAOYSA-N 0.000 description 2
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000003921 oil Substances 0.000 description 2
- 231100000614 poison Toxicity 0.000 description 2
- 230000007096 poisonous effect Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 235000009566 rice Nutrition 0.000 description 2
- 229910052709 silver Inorganic materials 0.000 description 2
- 239000004332 silver Substances 0.000 description 2
- 230000003746 surface roughness Effects 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 241001093269 Helicodiscus parallelus Species 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 240000002853 Nelumbo nucifera Species 0.000 description 1
- 235000006508 Nelumbo nucifera Nutrition 0.000 description 1
- 235000006510 Nelumbo pentapetala Nutrition 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 238000007545 Vickers hardness test Methods 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical compound [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000005137 deposition process Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000036541 health Effects 0.000 description 1
- 238000000713 high-energy ball milling Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 230000035800 maturation Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002905 metal composite material Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000007781 pre-processing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 239000011856 silicon-based particle Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
-
- 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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/05—Metallic powder characterised by the size or surface area of the particles
- B22F1/052—Metallic powder characterised by the size or surface area of the particles characterised by a mixture of particles of different sizes or by the particle size distribution
-
- 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
- B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
- B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
- B22F7/04—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/18—Layered products comprising a layer of metal comprising iron or steel
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/20—Layered products comprising a layer of metal comprising aluminium or copper
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B38/00—Ancillary operations in connection with laminating processes
- B32B38/18—Handling of layers or the laminate
-
- 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
- C23C24/02—Coating starting from inorganic powder by application of pressure only
- C23C24/06—Compressing powdered coating material, e.g. by milling
-
- 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
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/04—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge characterised by the coating material
- C23C4/06—Metallic material
- C23C4/08—Metallic material containing only metal elements
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2250/00—Layers arrangement
- B32B2250/03—3 layers
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2255/00—Coating on the layer surface
- B32B2255/06—Coating on the layer surface on metal layer
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2255/00—Coating on the layer surface
- B32B2255/20—Inorganic coating
- B32B2255/205—Metallic coating
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Composite Materials (AREA)
- Manufacturing & Machinery (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Plasma & Fusion (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention provides a multiphase dual-scale structural aluminum-tin (Al-Sn) based alloy powder/pure aluminum/steel backing composite bearing bush strip; the bearing bush strip comprises a three-layer structure composed of an upper-layer multiphase dual-scale structural Al-Sn based alloy layer, a middle-layer transition pure Al layer and a lower-layer low-carbon steel backing layer; the Al-Sn based alloy layer is an Al-Sn-Si-Mg-Cu mixed powder prepared by a mechanical alloying method and having a multiphase dual-scale structure, and is jointly composed of a nanocrystal Al-Sn-Si alloy powder, a micro coarse-crystal Al-Sn alloy powder and a nanocrystal Cu, Mg and Si and other trace elements. The invention also provides a preparation method of the multiphase dual-scale structural Al-Sn based alloy powder/pure aluminum/steel backing composite bearing bush strip; the preparation method adopts mechanical alloying, cold rolling and sintering processes; the processes comprise preparation of the multiphase dual-scale alloy powder, surface treatment of a steel backing, initial rolling composite, annealing, second re-rolling, sintering and the like. The mechanical-alloying prepared Al-Sn based bearing alloy problem produced in the bearing brush strip industrial application process is solved, and industrialization production is realized.
Description
Technical field
The invention belongs to powder metallurgically manufacturing technical field, it is related to the unleaded bearing shell of one kind mechanical alloy method synthesis and closes
Gold, substitute copper-lead axle bush band process technology with high intensity aluminium tinbase and in particular to a kind of double mesostructure aluminium tinbase of multiphase mixes
Close powder/fine aluminium/steel back composite bearing band and preparation method thereof.
Background technology
Develop to high-performance direction with automobile, engine is also to high rotating speed, high-power, low energy consumption, lightweight with high increase
Pressure direction is developed, and the bush material of automobile is also faced with high performance development.Simultaneously people for environmental protection consciousness with
And own health requires increasingly to improve, for poisonous lead element, the leaded of going in bearing shell product becomes inexorable trend.Therefore,
Research and development novel lead-free aluminium tinbase high intensity, high performance bush material come to substitute poisonous copper-lead axle bush material be when previous item carve
Do not allow slow task.
At present, on market, the al-sn bearing metal of main flow is usually used casting method acquisition, typically has good surface
Performance.But there is the subject matter of two aspects by the al-sn alloy that obtains of casting: the intensity of (1) alloy (hv30～
50) relatively low, the very difficult satisfaction currently demand to bearing shell high intensity；(2) easily produce serious gravity segregation in casting process
The problems such as.In order to overcome the problems referred to above, it is a kind of method effectively improving the strength of materials that mechanical alloying obtains nanometer crystalline phase；With
When, the double mesostructure of multiphase can be coordinated and tribological property with " hardness-toughness " of Effective Regulation alloy.But, existing market
The bush strip of upper use is all to be composited with steel back by casting the aluminium alloy plate obtaining, and closes with regard to aluminium tin both at home and abroad
Bronze becomes the maturation process of bush strip less with steel back composite rolling.
U.S.'s us 200300129721a1 patent of invention discloses a kind of side of powder sintered preparation aluminium base bush strip
Method, pure to acieral powder and two-layer al paper tinsel composite rolling is become the band of sandwich structure by the method first, through oversintering it
Afterwards, then with low carbon steel plate it is combined, after heat treatment make bush strip.But the alloy powder that this invention is used is common pure
Coarse-grain powder, and alloy powder and the compound of steel back employ two-step method, and it is not belonging to the multiphase involved by patent of the present invention
Double mesostructure aluminium tin mixed-powders and the direct combination technique of steel back.
Cn 201110090773.x patent of invention discloses a kind of double mesostructure aluminium tinbase of mechanical alloying preparation two-phase
The method of bearing metal, the method passes through high-energy ball milling, and repressed sintering obtains the double mesostructure aluminium kamash alloy of multiphase, made
Standby its hardness of al-sn alloy and tribological property all obtain large increase, but this invention is based only upon the system of al-sn alloy block
Standby, not yet alloy group element is used and carry out Rolling compund with steel back and make bush strip up.
Cn 00110680.5 patent of invention discloses a kind of manufacture method of bimetal band with steel substrate, and the method is using fast
Fast deposition+continuous rolling method, the atomized flow of semi-liquid metal or alloy is deposited to and is rolled on the steel band of continuous moving
Compound, make double metal composite strip.The method leads to the atomization aluminium alloy stream of semi liquid state serious oxygen in deposition process
Change problem, directly affects the raising of alloy strength.
U.S. us 04301213 and us 5053286 patent individually disclose aluminium tin ingot casting and aluminium with casting method preparation
Lead casting and the complex method of steel back, invent the gravity segregation problem that all there is aluminium tin and Al-Pb alloy for above-mentioned two, impact is closed
Golden mechanics and the raising of tribological property.
Cn 03116518.4 patent of invention discloses the preparation method of Noral/bimetal copper-steel composite, should
Method adopts hot rolled coil steel band to produce double metallic composite material, include the compound coil band of bimetallic, the preparation of mock silver band,
Bimetallic coil material or web continuous solid phase composite rolling.But the mock silver layer that this invention is obtained yet suffers from gravity segregation
The problems such as high with intensity.
Cn 1539634a patent of invention discloses a kind of method for preparing composite material of noral/steel bimetal, should
Method first prepares aluminium tinbase ingot casting with induction melting furnace, is carrying out method hot rolling, whole process pole with fine aluminium and steel back respectively
It is complicated, and process costs are higher, and surface easily aoxidizes.
At present, it is mainly by the method that powder obtains bush strip with steel back direct combination (powder plate is combined) and apply
In cu-pb bearing shell, its process is simple, alloy-layer microscopic structure easily regulates and controls.But, for al-sn bearing shell, main employing is cast
The aluminium kamash alloy made is combined with steel back, and this leads between powder and powder, powder and steel back mainly due to the oxidizable of aluminium
Sintering character is poor, and bond strength is not good, and there is mechanical alloying and prepare the work in bush strip for the al-sn base bearing alloy
In industry application process, produced tripartite's surface technology is not enough: (1) manocrystalline powders hardness is high, and poor fluidity is it is difficult to roll with steel back
System is compound；(2) because al powder particles are oxidizable it is difficult to use hot-rolling method, meanwhile, cold rolling but be difficult to obtain with steel back higher
Bond strength；(3) al powder particles surface easily absorbs water, and produces more bubble, have a strong impact on alloy-layer in clad-rolling process
The problems such as bond strength and steel back between.
Content of the invention
The object of the invention is mainly passed through the double mesostructure aluminium kamash alloy powder/fine aluminium/steel back of multiphase of the present invention and is combined
Bush strip and preparation method thereof, solves mechanical alloying and prepares the commercial Application in bush strip for the al-sn base bearing alloy
During produced tripartite's surface technology not enough it is achieved that industrialization production during commercial Application.
The invention provides a kind of double mesostructure aluminium kamash alloy powder/fine aluminium/steel back composite bearing band of multiphase, institute
State bush strip include low by the double mesostructure al-sn based alloy layer of multiphase on upper strata, middle transition pure al layer and lower floor
The three-decker of carbon steel backing layer composition；
Described al-sn based alloy layer is using Mechanical Alloying preparation, double mesostructure that have multiphase al-
Sn-si-mg-cu mixed-powder, its composition is by nanocrystalline al-sn-si alloy powder+micron coarse-grain al-sn alloy powder+receive
The brilliant micro constituent element of cu, mg, si of rice collectively forms；
The mass percent of described al-sn-si-mg-cu mixed-powder composition is: 12% sn, 0.5～3.5% si,
0.15～1.0% mg, and 0.2～2.0% cu reinforced alloys element, balance of al；
Described middle transition pure al layer is 50～200 μm prepared using heat spraying method of pure al layer；
Described low-carbon (LC) steel back layer is to have preferable toughness and the low-carbon alloy steel compared with high bearing capacity.
A kind of double mesostructure aluminium kamash alloy powder/fine aluminium/steel back composite bearing band of multiphase of the present invention, its
It is further characterized in that:
Described middle transition pure al layer, or be combined using the Direct Rolling of pure al paper tinsel and steel back.
The step of the pure al layer preparation method of described thermal spraying is:
(1), sandblasting is carried out to the steel back surface of pretreatment using 40～100# sand；
(2), pre-oxidized after standing 12h, directly carry out spraying pure al layer；
(3) and then made annealing treatment under 300 DEG C of furnace temperature.
The step that the described Direct Rolling using pure al paper tinsel and steel back is combined is:
(1), using 100# sand, is polished in the low-carbon (LC) steel back layer surface of pretreatment；
(2), pure al paper tinsel direct cold rolling thick with the 0.4mm of composite surface polishing again is combined, and deflection is 40～50%；
(3) and then made annealing treatment under 300 DEG C of furnace temperature.
Present invention also offers a kind of double mesostructure aluminium kamash alloy powder/fine aluminium/steel back composite bearing band of multiphase
Preparation method, this preparation method adopts mechanical alloying+cold rolling+sintering process, and technique includes the double yardstick alloyed powder of multiphase
Preparation, the surface treatment of steel back, first Rolling compund, annealing, secondary roll again and sintering process, concrete technology step is as follows:
Step (1), prepare the al-12%sn-si alloy powder of nanostructured using mechanical alloying, then with without
Micro mg, cu, si element mixing of the nanocrystalline structure of the micron coarse-grain al-12%sn powder of ball milling and pretreatment, obtains
There is the al-12%sn-si-mg-cu mixed-powder of the double yardstick composite construction of multiphase；
Step (2), prepared on pretreated mild steel back surface using flame spraying method thickness be 50～200
μm pure al layer, then the low carbon steel plate with pure al layer is made annealing treatment under 300 DEG C of furnace temperature；
Described step (2) or made on pretreated mild steel back surface using pure al paper tinsel and steel plate rolling complex method
For going out the pure al layer that thickness is 50～200 μm, then the low carbon steel plate with pure al layer is carried out at annealing under 300 DEG C of furnace temperature
Reason；
Step (3), scribble the steel plate of pure al layer using thermal jet as steel back, by double for described multiphase mesostructure mixed-powders
Equably it is laid in the pure al surface of steel back, thickness is 1～2mm, is rolled for the first time with the 5～15% of bulk deformation amount, obtains
Obtain bush strip green compact；
Described step (3) or have the steel plate of pure al layer as steel back rolling, by double for described multiphase mesostructure mixing
Powder is equably laid in the pure al surface of steel back, and thickness is 1～2mm, is rolled for the first time with the 5～15% of bulk deformation amount
System, obtains bush strip green compact；
Step (4), described bush strip green compact are made annealing treatment: band green compact are placed in vacuum drying oven, take out true
Sky, to 0.08～0.008pa, is subsequently passed argon gas, is incubated 1 hour when 100 DEG C, then with the slow heating of 2～5 DEG C/min speed
To 250～300 DEG C and be incubated 1 hour, along with the furnace cooling；
Step (5), by step (4) make annealing treatment after band blank carry out secondary cold roll again, bulk deformation amount be 5～
10%；
Step (6), by step (5) roll after band blank carry out vacuum-sintering: band blank is placed in vacuum drying oven,
It is evacuated down to 0.008～0.08pa, be subsequently passed argon gas, then with the slow progressive solution of 2～5 DEG C/min speed, respectively at 200 DEG C
Insulation each with 400 DEG C 1 hour, finally heated to 500～600 DEG C and be incubated 1 hour, along with the furnace cooling.
The present invention carries out composite rolling using multiphase double yardstick al-sn systems mixed-powder with the steel back being compounded with pure al layer,
On the one hand, due to the introducing of the soft phase coarse-grain powder of soft, effectively enhance the mobility of al-sn system powder and raising is received
The brilliant plasticity of rice, toughness, are conducive to the carrying out of Rolling compund；By the introducing of different coarse-grain contents, the hardness of al-sn matrix alloy
Freely can regulate and control with the range of 20～90hv.On the other hand, alloying element si, mg and cu element strengthens agglomeration, further
Improve tribological property: the introducing of (1) si element can promote sintering process to form al-si eutectic phase, breaks the netted of sn phase
In structure, and alloy, the si particle of Dispersed precipitate can carry heavy alloyed fatigue strength.This is mainly due to al-si against eutectic
Reaction temperature is 577 DEG C, and the al-sn-si alloy that mechanical alloying is obtained, its al-si can be following against eutectic reaction temperature
Drop to 540 DEG C about, promote the forming amount of eutectic liquid phase in sintering process, thus putting forward heavy alloyed consistency；Meanwhile, al-
Si eutectic phase inhibits al-sn divorsed eutectic again so that sn phase becomes more fine uniform distribution it is clear that this form will be favourable
In the raising of alloy mechanics and tribological property, this also illustrates that si can play the effect improving al-sn alloy microstructure；
(2) mg element passes through and al particle surface aoxidizes film reaction and forms mgal2o4Etc. phase, increase al-sn Alloy Wetting and reduce
Al/al interface energy, had both significantly improved the sintered density of alloy, was obviously improved distribution in al matrix for the sn phase again.But, mistake
The mg of amount leads to a large amount of mg2Sn and mg17al12Low-alloyed sintered density and tensile strength, can drop in the formation of mesophase；Experiment
Result shows, the double optimal mg needed for mesostructure al-sn alloy of multiphase that coarse-grain content is respectively 70%, 30% and 10% contains
Amount is respectively no higher than 0.5,1.0 and 1.2wt% respectively；(3) cu constituent element has preferable plasticity, is conducive to roll forming, with
When cu add the formation that again increased al-cu phase, the intensity not only having strengthened alloy reduces si again and adds the stress cracking leading to
Problem.
Brief description
Fig. 1 is the double yardstick aluminium kamash alloy/fine aluminium/steel-backed bearing band process chart of multiphase
Fig. 2 is the double yardstick aluminium kamash alloy/fine aluminium/steel-backed bearing band artwork of multiphase
Fig. 3 is the double yardstick aluminium kamash alloy/fine aluminium/steel-backed bearing band sintering process figure of multiphase
Fig. 4 is the double yardstick aluminium kamash alloy/fine aluminium of the multiphase/steel-backed bearing band cross section tissue gold of embodiment 2 preparation
Phasor；
Fig. 5 is the microcosmic of the double yardstick aluminium kamash alloy/fine aluminium/steel-backed bearing band alloy-layer of multiphase of embodiment 2 preparation
Tissue metallograph；
Fig. 6 is that the double yardstick aluminium kamash alloy/fine aluminium/steel-backed bearing band of multiphase of embodiment 4 preparation is bent into bearing shell in fact
Thing figure
In figure, the 1. double yardstick aluminium tin-base alloy layer of multiphase, 2. middle transition pure al layer, 3. low-carbon (LC) steel back layer.
Specific embodiment
The present invention is described in detail with reference to the accompanying drawings and detailed description.
The preparation technology flow process of the double mesostructure aluminium tin/fine aluminium/steel bush strip of multiphase of the present invention, as shown in figure 1, this system
Preparation Method adopts mechanical alloying+cold rolling+sintering process, and technique includes the preparation of the double yardstick alloyed powder of multiphase, the surface of steel back
Process, first Rolling compund, annealing, secondary roll and sinter etc. technique again, concrete technology step is as follows:
Step (1), prepare the al-12%sn-si alloy powder of nanostructured using mechanical alloying, then with without
Micro mg, cu, si element mixing of the nanocrystalline structure of the micron coarse-grain al-12%sn powder of ball milling and pretreatment, obtains
There is the al-12%sn-si-mg-cu mixed-powder of the double yardstick composite construction of multiphase；
Step (2), prepared on pretreated mild steel back surface using flame spraying method thickness be 50～200
μm pure al layer, then the low carbon steel plate with pure al layer is made annealing treatment under 300 DEG C of furnace temperature；
Described step (2) or made on pretreated mild steel back surface using pure al paper tinsel and steel plate rolling complex method
For going out the pure al layer that thickness is 50～200 μm, then the low carbon steel plate with pure al layer is carried out at annealing under 300 DEG C of furnace temperature
Reason；
Step (3), scribble the steel plate of pure al layer using thermal jet as steel back, by double for described multiphase mesostructure mixed-powders
Equably it is laid in the pure al surface of steel back, thickness is 1～2mm, is rolled for the first time with the 5～15% of bulk deformation amount, obtains
Obtain bush strip green compact；
Described step (3) or have the steel plate of pure al layer as steel back rolling, by double for described multiphase mesostructure mixing
Powder is equably laid in the pure al surface of steel back, and thickness is 1～2mm, is rolled for the first time with the 5～15% of bulk deformation amount
System, obtains bush strip green compact；
Step (4), described bush strip green compact are made annealing treatment: band green compact are placed in vacuum drying oven, take out true
Sky, to 0.08～0.008pa, is subsequently passed argon gas, is incubated 1 hour when 100 DEG C, then with the slow heating of 2～5 DEG C/min speed
To 250～300 DEG C and be incubated 1 hour, along with the furnace cooling；
Step (5), by step (4) make annealing treatment after band blank carry out secondary cold roll again, bulk deformation amount be 5～
10%；
Step (6), by step (5) roll after band blank carry out vacuum-sintering: band blank is placed in vacuum drying oven,
It is evacuated down to 0.008～0.08pa, be subsequently passed argon gas, then with the slow progressive solution of 2～5 DEG C/min speed, respectively at 200 DEG C
Insulation each with 400 DEG C 1 hour, finally heated to 500～600 DEG C and be incubated 1 hour, along with the furnace cooling.
Best mode for carrying out an invention:
(1) (nanocrystalline proportion is for nanocrystalline nc al-12wt%sn-xwt%si (1.5≤x≤3.5) alloy powder
40～80wt% is optimal, and granularity is 10～40 μm)；
(2) (coarse-grain proportion is that 20～60wt% is optimal to micron coarse-grain cg al-12wt%sn alloy powder, and granularity is
20～80 μm)；
(3) the micro constituent elements such as nanocrystalline nc cu, mg of pre-processing (are refined using pendulum shake ball milling, granularity is 1 μm of left side
Right)；
(4) optimum thickness of transition pure al layer is 100 μm；
(5) the double mesostructure aluminium tinbase mixed-powder powdering thickness most preferably 1.5mm on steel back of multiphase.
Embodiment 1
The preparation of the double yardstick al-12%sn alloyed powder of step one, multiphase
(1) by granularity be 200 mesh, purity be 99.5% aluminium powder and glass putty by al-12%sn mass percent mix,
Under argon gas protection, ball milling is carried out using qm-2sp planetary ball mill, rotational speed of ball-mill is 150rpm/min, Ball-milling Time is 40h,
Ratio of grinding media to material is 20:1, obtains nc al-12%sn alloy powder；
(2) by granularity be 200 mesh, purity be 99.5% aluminium powder and glass putty uniformly mix by al-12%sn mass percent
Close, obtain cg al-12%sn alloy powder；
(3) by granularity be 200 mesh, purity be 99.5% magnesium powder argon gas protection under, using qm-2sp planetary type ball-milling
Machine carries out ball milling, and rotational speed of ball-mill is 250rpm/min, and Ball-milling Time is 2h, and ratio of grinding media to material is 20:1, the mg powder uniformly being refined
End；
(4) the above-mentioned mg powder obtaining nc al-sn powder, cg al-sn powder and pretreatment is uniformly mixed in proportion,
The mass percent of wherein mg powder is 1.0%, and remaining powder quality percentage is nc:cg=9:1, obtains the double yardstick of multiphase
Al-12%sn-1.0%mg alloy powder.
Step 2, steel back surface treatment
It is 2.5mm from thickness, the 08f steel of a width of 36mm, a length of 500mm is as substrate steel back.
(5) steel back is carried out and blasting treatment, to remove surface and oil contaminant and iron rust, to expose unsalted surface and increase table
Surface roughness, improves the bond strength between steel back and aluminum layer；
(6) adopt high speed flame spraying method, on even application in the steel back after blasting treatment, thickness is 100 μm pure
Al layer, sprayed on material isAluminium wire, obtains thermal spraying aluminum steel back；
(7) steel back being coated with pure al layer will be placed in vacuum drying oven, is evacuated down to 0.08pa, is subsequently passed argon gas,
It is incubated 1 hour at 100 DEG C, then be heated to 300 DEG C with 2 DEG C/min speed and be incubated 1 hour, along with the furnace cooling.
Step 3, first Rolling compund
(8) by evenly laid out for double for the multiphase described in step 2 mesostructure al-12%sn-1.0%mg mixed-powders in institute
State in thermal spraying aluminum steel back, powder thickness is 1.5mm；
(9) by double for described multiphase mesostructure aluminium kamash alloy powder/fine aluminium/steel back three-deckers, pass through at room temperature
Duo mill carries out Rolling compund, and rolling linear velocity is 3.0m/min, and rolling reduction is 10%, obtains the double mesostructure of multiphase
Aluminium tin/fine aluminium/steel bush strip green compact.
Step 4, breaking down annealing
(10) the bush strip green compact described in step 3 are placed in vacuum drying oven, are evacuated down to 0.02pa, are subsequently passed argon
Gas, is incubated 1 hour at 100 DEG C, then is heated slowly to 300 DEG C with 2 DEG C/min speed and is incubated 1 hour, along with the furnace cooling is (see figure
2)；
Step 5, secondary roll again
(11) bush strip after annealing described in step 4 is carried out secondary rolling by duo mill, rolling linear velocity is
3.0m/min, rolling reduction is 5%；
Step 6, sintering
(12) by described in step 5 secondary roll again after bush strip be placed in vacuum drying oven, be evacuated down to 0.02pa, subsequently
It is passed through argon gas, at 100 DEG C, is incubated 1 hour, then with 2 DEG C/min speed progressive solution, be incubated 1 respectively at 200 DEG C and 400 DEG C little
When, finally heated to 550 DEG C and be incubated 1 hour, along with the furnace cooling can (Fig. 3).
Embodiment 2
The present embodiment step is substantially the same manner as Example 1, except that nc al-sn powder, cg in step one (4)
Al-sn powder and the mg powder of pretreatment, according to the 0.5% of mass percent, remaining powder quality percentage is wherein mg
Nc:cg=7:3, obtains the double mesostructure al-12%sn-0.5%mg mixed-powder of multiphase.By double for described multiphase mesostructure
In the evenly laid out steel back in thermal spraying aluminum of al-12%sn-0.5%mg mixed powder, through first Rolling compund, annealing, secondary roll again
And sintering process, obtain the bush strip of the double yardstick aluminium kamash alloy/fine aluminium/steel back of multiphase.
The double yardstick aluminium kamash alloy/fine aluminium of multiphase of the present invention/steel-backed bearing band cross section tissue figure and microstructure gold
Phasor, is shown in Fig. 4 and Fig. 5.
Embodiment 3
The present embodiment step is essentially identical with embodiment 1,2, except that nc al-sn powder, cg in step one (4)
Al-sn powder and the mg powder of pretreatment, the mass percent wherein pressing mg powder is 0.5%, remaining powder quality percentage
For nc:cg=5:5, obtain the double mesostructure al-12%sn-0.5%mg mixed-powder of multiphase.By double for described multiphase mesostructure
In the evenly laid out steel back in thermal spraying aluminum of al-12%sn-0.5%mg mixed powder, through first Rolling compund, annealing, secondary roll again
And sintering process, obtain the bush strip of the double yardstick aluminium kamash alloy/fine aluminium/steel back of multiphase.
Embodiment 4
The present embodiment step is essentially identical with embodiment 1,2,3, except that the double mesostructure of multiphase closes in step one
Being prepared as of bronze:
(1) by granularity be 200 mesh, purity be 99.99% silica flour, argon gas protection under adopt the shimmy ball of qm-3c high speed
Grinding machine carries out ball milling refinement, and rotational speed of ball-mill is 1000rpm/min, and Ball-milling Time is 4h, and ratio of grinding media to material is 20:1；
(2) by granularity be 200 mesh, purity be silica flour after 99.5% aluminium powder, glass putty and refinement by al-12%sn-
2.5%si mass percent mixes, and carries out ball milling using qm-2sp planetary ball mill, rotational speed of ball-mill is under argon gas protection
150rpm/min, Ball-milling Time is 40h, and ratio of grinding media to material is 20:1, obtains nc al-12%sn-2.5%si alloy powder；
(3) by granularity be 200 mesh, purity be silica flour after 99.5% aluminium powder, glass putty and refinement by al-12%sn-
2.5%si mass percent uniformly mixes, and obtains cg al-12%sn-2.5%si powder；
(4) described nc al-sn-si powder and cg al-sn-si powder are uniformly mixed, be nc:cg according to mass percent
=7:3, obtains the double mesostructure al-12%sn-2.5%si mixed-powder of multiphase；
Again by evenly laid out for double for the multiphase obtaining mesostructure al-12%sn-2.5%si mixed-powders in thermal spraying aluminum steel
Back, through first Rolling compund, annealing, secondary roll again and sintering process, obtain the double yardstick aluminium kamash alloy/fine aluminium/steel of multiphase
The bush strip of the back of the body.
The double yardstick aluminium kamash alloy/fine aluminium/steel-backed bearing band of multiphase of embodiment 4 preparation is bent into bearing shell such as figure in kind
Shown in 6.
Embodiment 5
The present embodiment step is essentially identical with embodiment 1,2,3, except that in step one (3): granularity is 200
Mesh, purity be 99.5% copper powder argon gas protection under, ball milling is carried out using qm-2sp planetary ball mill, rotational speed of ball-mill is
250rpm/min, Ball-milling Time is 2h, and ratio of grinding media to material is 20:1, the cu powder uniformly being refined；Obtain nc al-sn by above-mentioned
The cu powder of powder, cg al-sn powder and pretreatment uniformly mixes in proportion, and wherein the mass percent of cu powder is 1.0%,
Remaining powder quality percentage is nc:cg=7:3, obtains the double yardstick al-12%sn-1.0%cu mixed-powder of multiphase.To be many
In the double evenly laid out steel back in thermal spraying aluminum of mesostructure al-12%sn-2.5%cu alloyed powder of phase, through first Rolling compund, move back
Fiery, the secondary bush strip rolling again and sintering process, obtaining the double yardstick aluminium kamash alloy/fine aluminium/steel back of multiphase.
Embodiment 6
The present embodiment step is substantially the same manner as Example 5, except that the double mesostructure alloyed powder of multiphase in step one
Be prepared as:
(1) by granularity be 200 mesh, purity be 99.99% silica flour, argon gas protection under adopt the shimmy ball of qm-3c high speed
Grinding machine carries out ball milling refinement, and rotational speed of ball-mill is 1000rpm/min, and Ball-milling Time is 4h, and ratio of grinding media to material is 20:1；
(2) by granularity be 200 mesh, purity be silica flour after 99.5% aluminium powder, glass putty and refinement by al-12%sn-
2.5%si mass percent mixes, and carries out ball milling using qm-2sp planetary ball mill, rotational speed of ball-mill is under argon gas protection
150rpm/min, Ball-milling Time is 40h, and ratio of grinding media to material is 20:1, obtains nc al-12%sn-2.5%si alloy powder；
(3) by granularity be 200 mesh, purity be 99.5% aluminium powder and glass putty uniformly mix by al-12%sn mass percent
Close, obtain cg al-12%sn powder；
(4) by granularity be 200 mesh, purity be 99.5% magnesium powder argon gas protection under, using qm-2sp planetary type ball-milling
Machine carries out ball milling, and rotational speed of ball-mill is 250rpm/min, and Ball-milling Time is 2h, and ratio of grinding media to material is 20:1, the mg powder uniformly being refined
End；
(5) the mg powder of described nc al-sn-si powder, cg al-sn powder and micronization processes is uniformly mixed in proportion
Close, wherein the mass percent of mg powder is 0.5%, and remaining powder quality percentage is nc:cg=7:3, obtain the double chi of multiphase
Degree structure al-12%sn-1.8%si-0.5%mg mixed-powder；
(6) by evenly laid out for double for described multiphase mesostructure al-12%sn-1.8%si-0.5%mg mixed-powders in heat
Spraying aluminum steel back, through first Rolling compund, annealing, secondary roll again and sintering process, obtain multiphase pair yardstick aluminium kamash alloy/
The bush strip of fine aluminium/steel back.
Embodiment 7
The present embodiment step is essentially identical with embodiment 4,5,6, except that the double mesostructure of multiphase mixes in step one
Close being prepared as of powder:
(1) by granularity be 200 mesh, purity be 99.99% copper powder and silica flour, according to 1:1 argon gas protection under adopt qm-
3c high speed vibration ball mill carries out ball milling refinement, and rotational speed of ball-mill is 1000rpm/min, and Ball-milling Time is 4h, and ratio of grinding media to material is 20:1；
(2) by granularity be 200 mesh, purity be copper silicon composite powder after 99.5% aluminium powder, glass putty and refinement by al-12%
Sn-1.5%si-1.5%cu mass percent mixes, and carries out ball milling using qm-2sp planetary ball mill under argon gas protection,
Rotational speed of ball-mill is 150rpm/min, and Ball-milling Time is 40h, and ratio of grinding media to material is 20:1, obtains nc al-12%sn-1.5%si-
1.5%cu alloy powder.
(3) by granularity be 200 mesh, purity be copper silicon composite powder after 99.5% aluminium powder, glass putty and refinement by al-12%
Sn-1.5%si-1.5%cu mass percent uniformly mixes, and obtains cg al-12%sn-1.5%si-1.5%cu powder；
(3) obtain, by above-mentioned, the mg that nc al-sn-si-cu powder, cg al-sn-si-cu powder and pre- ball-milling treatment are crossed
Powder uniformly mixes in proportion, and wherein the mass percent of mg powder is 0.5%, and remaining powder is nc:cg according to mass percent
=7:3, obtains the double mesostructure al-12%sn-1.5si%-1.5%cu-0.5%mg mixed-powder of multiphase；
(4) will be uniform for double for described multiphase mesostructure al-12%sn-1.5si%-1.5%cu-0.5%mg mixed-powders
Be laid in thermal spraying aluminum steel back, through first Rolling compund, annealing, secondary roll again and sintering process, obtain the double yardstick aluminium of multiphase
The bush strip of kamash alloy/fine aluminium/steel back.
Embodiment 8
The present embodiment step is substantially the same manner as Example 2, except that the process of steel back:
It is 2.5mm from thickness, the 08f steel of a width of 36mm, a length of 500mm is as substrate steel back.
(1) steel back is carried out and blasting treatment, to remove surface and oil contaminant and iron rust, to expose unsalted surface and increase table
Surface roughness, improves the bond strength between steel back and aluminum layer；
(2) is polished using 100# sand in the steel back surface of pretreatment, (composite surface is for thick pure al paper tinsel with 0.5mm
Polishing) direct cold rolling be combined, wherein deflection be 40～50%；
(3) the above-mentioned steel back being compounded with pure al layer is placed in vacuum drying oven, is evacuated down to 0.08pa, is subsequently passed argon gas,
It is incubated 1 hour at 100 DEG C, then be heated slowly to 300 DEG C with 2 DEG C/min speed and be incubated 1 hour, along with the furnace cooling；
(4) by evenly laid out for double for described multiphase mesostructure al-12%sn-0.5%mg mixed-powders in thermal spraying aluminum steel
Back, through first Rolling compund, annealing, secondary roll again and sintering process, obtain the double yardstick aluminium kamash alloy/fine aluminium/steel of multiphase
The bush strip of the back of the body.
Table 1
Embodiment 1 arrives hardness and the friction of the double yardstick bush strip of multiphase prepared by embodiment 8 and industrial bush strip
Polishing machine result is as shown in table 1.Vickers hardness test condition: load 4.9n, dwell time 10s.Dry sliding wear condition: carry
Lotus 100n, rotating speed 214rpm/min, wearing- in period 1h.As it can be seen from table 1 the double yardstick aluminium tin of the multiphase of present invention preparation/pure
Aluminium/steel bush strip, its hardness is significantly higher than industrial a17x bush strip, meet engine at a high speed, the sending out of high-mechanic direction
Exhibition；Its wear resistant friction reducing performance is also better than industrial a17x bush strip simultaneously.
Above-mentioned embodiment is an example of the present invention, is not intended to limit enforcement and the interest field of invention, all
The equivalence changes made according to the content described in the present patent application scope of patent protection and modification, all should be included in the present patent application
In the scope of the claims.
Claims (5)
1. a kind of double mesostructure aluminium kamash alloy powder/fine aluminium/steel back composite bearing band of multiphase is it is characterised in that described
Bush strip is included by the low-carbon (LC) of the double mesostructure al-sn based alloy layer of multiphase, middle transition pure al layer and lower floor on upper strata
The three-decker of steel back layer composition；
Described al-sn based alloy layer is using Mechanical Alloying preparation, double mesostructure that have multiphase al-sn-
Si-mg-cu mixed-powder, its composition is by nanocrystalline al-sn-si alloy powder+micron coarse-grain al-sn alloy powder+nanocrystalline
The micro constituent element of cu, mg, si collectively forms；
The mass percent of described al-sn-si-mg-cu mixed-powder composition is: 12% sn,
0.5～3.5% si, 0.15～1.0% mg, and 0.2～2.0% cu reinforced alloys element, balance of al；
Described middle transition pure al layer is 50～200 μm prepared using heat spraying method of pure al layer；
Described low-carbon (LC) steel back layer is to have preferable toughness and the low-carbon alloy steel compared with high bearing capacity.
2. the double mesostructure aluminium kamash alloy powder/fine aluminium/steel back compound-axis controlling of a kind of multiphase according to claim 1
Material it is characterised in that: described middle transition pure al layer, or be combined using the Direct Rolling of pure al paper tinsel and steel back.
3. the double mesostructure aluminium kamash alloy powder/fine aluminium/steel back compound-axis controlling of a kind of multiphase according to claim 1
Material is it is characterised in that the step of described thermal spraying pure al layer preparation method is:
(1), sandblasting is carried out to the steel back surface of pretreatment using 40～100# sand；
(2), pre-oxidized after standing 12h, directly carry out spraying pure al layer；
(3) and then made annealing treatment under 300 DEG C of furnace temperature.
4. the double mesostructure aluminium kamash alloy powder/fine aluminium/steel back compound-axis controlling of a kind of multiphase according to claim 2
Material is it is characterised in that the step that the described Direct Rolling using pure al paper tinsel and steel back is combined is:
(1), using 100# sand, is polished in the low-carbon (LC) steel back layer surface of pretreatment；
(2), pure al paper tinsel direct cold rolling thick with the 0.4mm of composite surface polishing again is combined, and deflection is 40～50%；
(3) and then made annealing treatment under 300 DEG C of furnace temperature.
5. the preparation method of the double mesostructure aluminium kamash alloy powder/fine aluminium/steel back composite bearing band of a kind of multiphase, its feature
It is, this preparation method adopts mechanical alloying+cold rolling+sintering process, technique includes the preparation of the double yardstick alloyed powder of multiphase, steel
The back of the body surface treatment, first Rolling compund, annealing, secondary roll again and sintering process, concrete technology step is as follows:
Step (1), prepare the al-12%sn-si alloy powder of nanostructured using mechanical alloying, then with without ball milling
Micron coarse-grain al-12%sn powder and pretreatment nanocrystalline structure the mixing of micro mg, cu, si element, acquisition has
The al-12%sn-si-mg-cu mixed-powder of the double yardstick composite construction of multiphase；
Step (2), prepare thickness on pretreated mild steel back surface using flame spraying method be 50～200 μm
Pure al layer, then makes annealing treatment under 300 DEG C of furnace temperature to the low carbon steel plate with pure al layer；
Described step (2) or prepared on pretreated mild steel back surface with steel plate rolling complex method using pure al paper tinsel
Thickness is 50～200 μm of pure al layer, then the low carbon steel plate with pure al layer is made annealing treatment under 300 DEG C of furnace temperature；
Step (3), scribble the steel plate of pure al layer using thermal jet as steel back, will be uniform for double for described multiphase mesostructure mixed-powders
Be laid in the pure al surface of steel back, thickness is 1～2mm, is rolled for the first time with the 5～15% of bulk deformation amount, obtains axle
Watt band green compact；
Described step (3) or have the steel plate of pure al layer as steel back rolling, by double for described multiphase mesostructure mixed-powders
Equably it is laid in the pure al surface of steel back, thickness is 1～2mm, is rolled for the first time with the 5～15% of bulk deformation amount, obtains
Obtain bush strip green compact；
Step (4), described bush strip green compact are made annealing treatment: band green compact are placed in vacuum drying oven, are evacuated down to
0.08～0.008pa, is subsequently passed argon gas, is incubated 1 hour when 100 DEG C, then is heated slowly to 250 with 2～5 DEG C/min speed
～300 DEG C and be incubated 1 hour, along with the furnace cooling；
Step (5), by step (4) make annealing treatment after band blank carry out secondary cold roll again, bulk deformation amount be 5～10%；
Step (6), step (5) is rolled after band blank carry out vacuum-sintering: band blank is placed in vacuum drying oven, takes out true
Empty be subsequently passed argon gas to 0.008～0.08pa, then with the slow progressive solution of 2～5 DEG C/min speed, respectively at 200 DEG C and
400 DEG C of each insulations 1 hour, finally heated to 500～600 DEG C and be incubated 1 hour, along with the furnace cooling.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410714427.8A CN104589726B (en) | 2014-12-01 | 2014-12-01 | Multiphase dual-scale structural aluminum-tin based composite bearing bush strip and preparation method thereof |
| PCT/CN2014/094865 WO2016086474A1 (en) | 2014-12-01 | 2014-12-24 | Multiphase dual-scale structural aluminum-tin base bonded bearing strip and preparation method thereof |
Applications Claiming Priority (1)
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| CN201410714427.8A CN104589726B (en) | 2014-12-01 | 2014-12-01 | Multiphase dual-scale structural aluminum-tin based composite bearing bush strip and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106498138A (en) * | 2016-10-20 | 2017-03-15 | 西安交通大学 | A kind of multiphase nano lamellar alloy material and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106399732B (en) * | 2016-09-27 | 2018-01-02 | 华南理工大学 | A kind of powder sintered method for preparing Al Sn base bearing alloy |
| CN109500400A (en) * | 2018-11-29 | 2019-03-22 | 鞍钢重型机械有限责任公司 | The production line and technique of metal powder and metal plate and belt composite rolling complex plate strip |
| CN112008084B (en) * | 2020-09-02 | 2022-05-10 | 宁波乌卡科技有限公司 | Preparation method and application of aluminum-iron composite material for machine arm |
| CN112522548B (en) * | 2020-11-06 | 2022-07-12 | 北京工业大学 | Wear-resistant Mg-containing aluminum-tin bearing bush alloy |
| CN114131028B (en) * | 2021-12-02 | 2024-04-05 | 广东省科学院新材料研究所 | Aluminum-based porous composite sandwich structure and preparation method and application thereof |
| CN115194294B (en) * | 2022-06-02 | 2023-10-24 | 东南大学 | Aluminum steel composite material and arc additive preparation method thereof |
| CN115351295B (en) * | 2022-08-26 | 2023-10-27 | 河北建筑工程学院 | Composite board preparation process |
| CN116987921A (en) * | 2023-09-28 | 2023-11-03 | 西安稀有金属材料研究院有限公司 | TiAl-based composite material with full-lamellar network structure and preparation method thereof |
| CN118237797A (en) * | 2024-05-27 | 2024-06-25 | 中国机械总院集团宁波智能机床研究院有限公司 | Aluminum-based bearing alloy welding wire and preparation method and application thereof |
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| GB1337265A (en) * | 1970-11-12 | 1973-11-14 | Glacier Metal Co Ltd | Aluminium based bearing materials |
| IL48735A0 (en) * | 1975-12-25 | 1976-02-29 | King Ltd | A method for the production of flanged parts for bearings |
| US4471029A (en) * | 1981-10-15 | 1984-09-11 | Taiho Kogyo Co., Ltd. | Al-Si-Sn Bearing Alloy and bearing composite |
| CN1157492C (en) * | 2000-07-19 | 2004-07-14 | 中国科学院金属研究所 | Process for preparing bimetal band with steel substrate |
| CN1231319C (en) * | 2003-10-28 | 2005-12-14 | 华南理工大学 | Method for producing bearing shell material of Nano clad aluminium base |
| CN1546878A (en) * | 2003-11-28 | 2004-11-17 | 东风汽车有限公司 | Bearing bush strip and production method thereof |
| CN102134661B (en) * | 2011-04-12 | 2012-08-08 | 华南理工大学 | Method for manufacturing multi-scale structure aluminum/stannum-based bearing alloy |
| CN102407625A (en) * | 2011-08-28 | 2012-04-11 | 十堰洪运轴承材料有限公司 | Aluminum base and steel double metal bearing bush novel material and production technology thereof |
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| CN106498138A (en) * | 2016-10-20 | 2017-03-15 | 西安交通大学 | A kind of multiphase nano lamellar alloy material and preparation method thereof |
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