CN105937004A - Aluminum alloy material replacing QT500 high-pressure square flange and gravity casting method of aluminum alloy material - Google Patents
Aluminum alloy material replacing QT500 high-pressure square flange and gravity casting method of aluminum alloy material Download PDFInfo
- Publication number
- CN105937004A CN105937004A CN201610493119.6A CN201610493119A CN105937004A CN 105937004 A CN105937004 A CN 105937004A CN 201610493119 A CN201610493119 A CN 201610493119A CN 105937004 A CN105937004 A CN 105937004A
- Authority
- CN
- China
- Prior art keywords
- aluminum alloy
- alloy
- high pressure
- casting
- pressure method
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
Abstract
The invention discloses an aluminum alloy material replacing a QT500 high-pressure square flange. The aluminum alloy material is characterized in that the aluminum alloy material is mainly prepared from, by weight percent, 0.15%-0.18% of nickel (Ni), not larger than 2% of manganese (Mn), 0.05%-0.5% of cadmium (Cd), 4.2%-8.0% or not smaller than 0.5% and not larger than 3% of cuprum (Cu), 1%*10<-4>-2.0% or 7.0%-9.0% of Lewis acid and alkali pairs and the balance Al; the percent of Cu is larger than or equal to 0.8Mn+4.05%, or the percent of Cu is larger than or equal to 0.5%, smaller than or equal to 3% and larger than or equal to 1.5Mn; and the average alloy grain size is made to be smaller than 120 micrometers.
Description
Technical field
The present invention relates to a kind of aluminum alloy materials substituting QT500 high pressure method orchid and preparation method thereof.
Background technology
Considerably beyond ferrum, (aluminum is 8.2wt% to aluminum stock number in the earth's crust, ferrum is 5.1wt%), and whole world iron and steel volume of production and marketing more than 1,200,000,000 tons every year, aluminum metal volume of production and marketing only has 0.55 hundred million tons, and this huge contrast fully reflects human society and the Resources and utilization level of aluminum and aluminum is lagged far behind the development of exploitation level to ferrous materials.
Spheroidal graphite cast-iron (abbreviation magnesium iron) is one of primary base material in steel industry, extensively it is heavily used for manufacturing stress complexity, intensity, toughness, wearability etc. require higher part, as universal machine, lifting, agricultural, automobile, cast, weave, lathe, electric power, petrochemical industry, boats and ships part etc., Main Morphology and type are hydraulic pressure housing, the pump housing, pipeline, valve body, cylinder body, wheel hub, shaft member, ball connection, driving member, suspender, hook fastener, conducting element, tumbler etc..
Spheroidal graphite cast-iron is of many uses, but spheroidal graphite cast-iron production manufacture needs to carry out at very high temperatures, corresponding energy consumption is the highest, pollutes big, and along with lightweight and the requirement of energy-conserving and environment-protective, relevant spheroidal graphite cast-iron product is in the urgent need to finding new succedaneum.
In the technology upgrading of " with aluminum for steel ", in order to give full play to aluminium alloy with " gently " serial advantageous characteristic as representative, must first make its aspect in " by force " have tremendous development, can not have unacceptable manufacturing cost increment simultaneously, could significantly expand its use field.This just requires first to make a breakthrough in Al-alloy material design.
The method close examination prepared from material, owing to material feature is by carry the functional combined contribution of microcosmic thing of this feature out, therefore good functional thing is obtained combined, such as high intensity, high-melting-point, high-ductility, high rigidity, corrosion-resistant etc., it it is the final result of various preparation method pursuit, thus, the Design of Chemical Composition of aluminium alloy and its technology of preparing also exist close internal integrity, this uniformity, in brief, it it is a kind of atom relation of how being combined into required " thing phase molecule ", the i.e. thing of material can regard a kind of molecular structure mutually as.nullThe mixed smelting of formula element and casting crystalline，It it is the major contributing link of fusion casting formation material thing phase molecule combinative structure，In fusion-casting process，Solid solution crystal grain determines crystalline state combination (submicron particles: about yardstick 10～300 μm) of alloy mutually with the intermetallic compound molecule thing of crystal boundary，Subsequent heat treatment or flow harden are then that the precise and tiny structure (Subnano-class or sub-micron grade particle: yardstick 10nm～＜ 1 μm) to fine structure under crystalline state group frame (micron particles: about yardstick 1～30 μm) or even more microcosmic is adjusted and perfect，This adjustment and perfect degree and scope，In known technology and traditional view，Think mainly by the combined decision of thing that the alloy phase diagram region residing for alloy composition is given，But，Alloy phase diagram does not provide the interpolation of other trace element and gets rid of the impact produced，Add with less prediction and get rid of the directiveness that thing is affected by other trace element mutually.Theory and the method for using for reference alloy solution chemistry improve melt structure; the covering of such as protecting film; the interpolation of slag former, refining agent or alterant; degasification slag removal and purification etc.; it is to improve the combination of alloy crystalline state, fine structure or even the important technical of the more precise and tiny structure of microcosmic; but these means, owing to being to grope accumulation during preparing alloy to get, are therefore often considered as " preparation technology " rather than the part of " composition design ".
On engineer applied, the size of aluminum alloy solution body crystal grain and state, and it is distributed in the size and form of the intermetallic compound of crystal boundary, the mechanical property of alloy there is is conclusive impact.Thick plane is brilliant, dendrite, the irregular crystals such as column crystal and the thick brittle property intermetallic compound being distributed in crystal boundary, the obdurability contribution of matrix all can be balanced out by fine structure good for alloy and precise and tiny structure, because the law of development that these coarse grains are deferred to results from the raw core of type wall of casting mold cavity, from the growth pattern that export-oriented liquid internal is unidirectionally extended, cause the component segregation of alloy, crystallize thick unidirectional, the defect that macro property is uneven, thus become some common deficiencies of alloy, such as pin hole, pore, shrinkage cavity, shrinkage porosite, segregation, thick solid solution, high hardness compound, the root of crackle etc..The routine used at present goes bad the means of means and crystal grain thinning, as added aluminum titanium boron or Al-Ti-C master alloy, best effect can only make mean grain size refine to 120～150 microns, and the form of dendrite does not often have basic transformation, this is the important bottleneck problem that alloy mechanical property improves.Because for aluminium alloy, it is thus achieved that the refinement of the approach that intensity and toughness improve, only crystal grain and rounding simultaneously；The adjustment of Technology for Heating Processing, at crystalline structure it has been determined that, intensity or one aspect of toughness can only be made to obtain and to optimize.Therefore, refine the most further and the mean grain size of rounding alloy, be the target pursued all the time of industrial circle.
In terms of design of material angle, 211Z material there is also some problems being difficult to overcome.Micro analysis finds, has some bulky grains to have the highest titanium Ti and rare earth concentration, and as the material for promoting crystal grain to refine, this phenomenon shows that Ti and rare earth have moved towards to need the opposite of solution problem；And in the production process of 211Z alloy-steel casting, also there is defect common as common aluminum alloy, including pin hole, pore, shrinkage cavity and porosity, segregation, thick solid solution, high hardness compound, be mingled with (slag), cold shut, cold shot, crackle, rotten defect, solid solution deficiency and burning etc..
These defects, main cause still to be started with from the microcosmic phase structure of the chemical composition of alloy itself and formation thereof and be studied, especially the formation mechenism of thing phase molecule combinative structure is furtherd investigate, just can see clearly essence, and then find solution problem, the effective way of elimination defect.
Analyze by aluminum bronze manganese systems (Al-Cu-Mn) alloy being up to spherical aberration correction scanning transmission electron microscope (STEM) the precise and tiny constituency of the very high resolution of 0.08nm, it is thus achieved that set up various phase structures on an atomic scale, Atomic Resolution and chemical element distribution.Confirm wherein to there is a series of hardening constituent, including well-known Al-Cu binary metastable phase (GP district, θ ＂, θ ＇), new disc phase and balance phase θ (Al2Cu)；Wherein inside matrix grain, new discovery one rod forked (T+ θ H) combination phase, the trunk portion T-phase of this combination phase is Al-Cu-Mn ternary phase, molecular structural formula Al20Cu2Mn3, molecule phase character be diameter about 100nm, length about 600～1000nm be mandrel shape and its (010) face and alloy matrix aluminum { 010} face coherence；And apposition growth size is compared with the Al-Cu binary secondary phase of big (thickness about 20nm, be about 50nm) around T-phase, owing to this secondary phase compares with other Al-Cu metastable phase in matrix (GP district, θ ＂, θ ＇ or other disc phase), structurally there is very big difference, particularly thickness is thicker much than other Al-Cu metastable phase, therefore the present invention is referred to as θ H phase, its molecular structural formula AlxCu (x is likely less than 2), is a kind of rich Cu molecule.
Theoretical according to alloy strengthening, the intensity of alloy is material median surface or dislocation movement by slip is produced by the obstruction of particle, hinders the strongest, and the intensity of material is the biggest.And particle hinders the result that behavior interacts with material median surface or dislocation movement by slip, there are two kinds: one is when the strong hardness of particle own is not high enough, dislocation will cut through particle and continue sliding, another kind is that particle intensity is the highest, dislocation cannot cut through, then can only walk around particle and continue sliding, and around particle, leave a circle dislocation ring.
The size that the strength of materials is contributed by two kinds of results is apparent from: it is bigger to the contribution of the strength of materials than cutting through particle to walk around particle；Cutting through particle can provide material preferable elongation percentage, and walks around particle due to the potentiation of dislocation ring, it will thus provide the higher yield strength of material and tensile strength.
Aluminum alloy square flange the most also has correlational study, because the limitation of basic material, its mechanical property is relatively low, and especially tensile strength and welding performance is poor, has had a strong impact on the life-span of square flange, adds use cost and security risk.
Summary of the invention
The technical problem to be solved in the present invention is: provide a kind of and substitute blue aluminum alloy materials of QT500 high pressure method and preparation method thereof, wherein add Lewis Acids and Bases pair, effectively to expedite the emergence of critical nucleus (obtaining equiax crystal), alloy is made to obtain the optimal combined structure of molecule thing ((T+ θ H) combines phase) before curing, promote alloy crystalline state optimization, enable aluminum alloy to base material and realize 500MPa and higher strength grade, thus reach to produce the Al-alloy products substituting QT500 high pressure method orchid.
The technical scheme is that: a kind of aluminum alloy materials substituting QT500 high pressure method orchid, main constituent content is by weight percentage: nickel: 0.15%-0.18%, manganese Mn :≤2%, cadmium Cd:0.05%～0.5%, copper Cu:4.2%～8.0% and Cu >=0.8Mn+4.05% or copper 0.5%≤Cu≤3% and Cu >=1.5Mn；Lewis Acids and Bases, to total amount 1% × 10-4～2.0% or 7.0%～9.0%, makes alloy mean grain size ＜ 120 microns, and surplus is aluminum Al.
Described alloy grain is equiax crystal.
In described alloy grain, sub-nanometer (T+ θ H) combination phase amount reaches >=1/square micron.
One in the described Lewis Acids and Bases positive and negative ion body to being combined into for metal and part, complicated ligand compound, super large heteropoly compound, metal halogen compound, main group dvielement, interior transition dvielement, or more than one mixing.
Cation body, anion body that described metal and part are combined into comprise four cyano cadmium anion body [Cd (CN)4]2 -。
Described complicated ligand compound or super large heteropoly compound comprise hexafluoro and close potassium silicate K2[SiF6]。
Described Lewis Acids and Bases pair, accounts for Al matrix percentage by weight by element addition, and scope is: Cr ＜ 0.5%, Bi ＜ 0.1%, La ＜ 0.03%, K2[SiF6] ＜ 0.04%, CuCl3＜ 0.04%, [Cd (CN)4]2 -＜ 0.04%.
A kind of preparation method substituting the blue aluminum alloy materials of QT500 high pressure method, comprises the steps of
(1) in the range of aforementioned Lewis Acids and Bases is to, element ratio, selected one group of combinations of substances, determine weight ratio, the alloy total amount prepared as required, extrapolate the weight of every kind of required material；
(2) adding aluminium ingot or molten aluminum liquid in smelting furnace, heating is also incubated more than 700 DEG C；
(3) addition manganese Mn, cadmium Cd, copper Cu, nickel stirs, and adds selected Lewis Acids and Bases pair, or the Lewis Acids and Bases that addition is selected is to combination, stirs；
(4) then above-mentioned alloy melt is carried out furnace refining；
(5) remove the gred after refine, stand, sample analysis alloy composition, adjust chemical composition in the deviation range of regulation according to analysis result；Homoiothermic is to more than 650 DEG C, and aluminium alloy is come out of the stove, online degasification, slagging-off；
(6) casting: use gravity casting and pouring.
Described gravity casting and pouring, step is as follows:
1. pourable casting after filtering；
2. mould should be preheated before casting, install core, by compressed air, mold cavity is blown clean；
3. take manually to pour into a mould or automatization's cast, in stove, dip aluminium alloy with casting ladle and pour mould gate into and be full of die cavity by ingate；Natural cooling or the coldest；
4. product, natural cooling, cleaning core, sawing rising head, polishing overlap are taken out in die sinking；
5. appearance quality detection: rough casting, before carrying out presentation quality inspection, should be cleaned out smooth, the dead head of non-machined surface should be cleaned to cast(ing) surface and flush；
6. internal soundness detection；
7. solution treatment: solid solution furnace sent into by the blank that foundry goods completes roughing and inside and outside quality testing, carries out less than 560 DEG C solution treatment, quenches at once after being incubated, uses water-cooled or oil cold；
8. ageing strengthening: the foundry goods completing solution treatment is sent into aging furnace and carries out ageing strengthening process, ageing strengthening below 230 DEG C, after insulation, natural cooling of coming out of the stove；
9. sample analysis test checking；
10. Practical Performance checking.
Beneficial effects of the present invention: pointed by lewis' theory of acids and bases, molecule can be occurred in aluminium alloy melt to disintegrate or contribute in time nano-area " acid-base pair " material of thing phase molecule structure optimization (i.e. less than the scope of 1 nanometer), the fine structure being applied to melt nanoscale scope adjusts, and is the topmost creative technological means of the present invention.
By using lewis' theory of acids and bases, make about Lewis Acids and Bases the interpolation of trace element of carrying and eliminating, disintegrate at aluminium alloy melt environment generation molecule and convert, to provide abundant disturbance and the activation effect of (0.1nm～10nm range scale) in the hyperfine microcell of melt, reach to expedite the emergence of critical nucleus to be formed in a large number, alloy grain degree is made to be refined further, form more rounding；Optimize very small areas (micron order: about yardstick 1～30 μm) and the thing phase molecule combinative structure of precise and tiny region (Subnano-class or sub-micron grade particle: yardstick 10nm～＜ 1 μm) simultaneously, increase (T+ θ H) combination content in alloy substrate, be the mechanism problem of the alloy strengthening that the present invention solves.
One in the present invention aforementioned Lewis Acids and Bases positive and negative ion body to being combined into for metal and part, complicated ligand compound, super large heteropoly compound, metal halogen compound, main group dvielement, interior transition dvielement, or more than one mixing.
Such as, anion body [Cd (CN)4]2 -It is Louis's " acid-base pair ", the Cd that can accept electronics pair in material+Being lewis acid, the corresponding part-CN providing electronics pair is lewis base.
Cation body and anion body are as Louis " acid-base pair ", alloy grain refinement had the excellent effect that ordinary matter cannot realize, this is at normal temperatures can stable existence as normal material molecule due to: these gas ions, and occur molecule to disintegrate in aluminium alloy melt such high temperature acid or alkali environment, generate lewis acid and lewis base；Owing to being that molecule disintegrates, so being " falling apart " of the atom combinative structure of a kind of nanometer range, with gaseous exhaust out, the core metal ion discharged then reselects and combines other atom its ligand moiety.
This generation disintegration in aluminium alloy melt and reconstruct, dissolve different from common material, because: 1. decompose the incipient bubble only one of which molecular size of gaseous material formation of release under high temperature (less than 1nm, i.e. secondary nanophase), specific surface area is maximum, there is the disturbance ability of extremely strong activity and nanometer range, it is in the size range that crystallization critical nucleus is formed, the fluctuation of energy of atom in the melt superfinishing microcell caused therefrom, the states such as structure fluctuating and composition fluctuations rise and fall all with extremely strong Characteristics of Mutation, neighbouring more polyatom is promoted to cross over crystallization potential barrier, so being particularly conducive to a large amount of formation of critical nucleus, the catalysis of intermetallic compound reaction of formation and the refinement of alloy structure crystal grain are all created the good effect being better than common alterant such as aluminum titanium boron；This disturbance and activation effect in the superfinishing microcell of secondary nanometer range of positive and negative ion body simultaneously, is that the bubble (diameter is more than 0.5mm) that conventional additional purification gas is formed cannot realize；2. the metallic atom or the cation that decompose release have the volume less than part and bigger specific surface area, it is higher to disturbance and the activation effect of neighboring atom, the superfinishing microcell state caused rises and falls more significantly, the most higher to intermetallic compound reaction of formation catalysis and alloy substrate tissue Grain Refinement Effect；3. acid-base pair division in high-temperature fusant and reconstruct enhance particle in the dispersion of microcell and diffusion velocity, will not cause clustering as common metal or additive, and restrained effectively the alloying component segregation and the gathering of bulky grain particle caused because of additive and grow up, this can effectively solve conventional die fining agent tendency of coarsening in crystallization process, such as, can prevent the roughening of titanium Ti and rare-earth phase；4. part bubble can also occur secondary reaction, and after a series of changes, retinue purifies gas discharge melt and (such as generates CO2、CH4、N2、NH3Or H2S) or enter slag (such as Al2O3、Al(HO)3Or Al4C3), this purification, it is possible to most stable of solid-state or gaseous material, dissolving H in the melt and oxide impurity absorbs and decomposes, thus its purification is more preferable than conventional gas purification mode effect.Here it is positive and negative ion body is as the interpolation of Lewis Acids and Bases pair and eliminating, atom reconstruct in the disintegration of aluminium alloy melt environment generation molecule, acid-base chemical conversion and superfinishing microcell, with the abundant disturbance in offer melt superfinishing microcell and activation effect, reach to expedite the emergence of critical nucleus to generate in a large number and inhibiting grain growth effect, and realize the mechanism of more preferable clean-up effect.By this mechanism, making matrix crystalline state generally become equiax crystal, grain size is averagely less than 120 μm, and further effect of optimization can reach grain size averagely in 50～100 μm.This effect, is to use merely the gas purification technique of the conventional die fining agent such as aluminum titanium boron and aluminum titanium carbon and routine to realize.
Complicated ligand compound, super large heteropoly compound are as Lewis Acids and Bases pair, alloy grain refinement also had the good result that ordinary matter cannot realize, because their molecular structure is similar with the structure of positive and negative ion body, atom reconstruct in the disintegration of molecule, acid-base chemical conversion and superfinishing microcell can occur in the such environment of aluminium alloy melt, also can discharge the part of gaseous state or liquid when molecule disintegrates, after series reaction, retinue purifies gas discharge melt and (such as generates CO2、CH4、N2、NH3Or H2S) or enter slag (such as NaCl, KCl, Al (HO)3、Al2O3Or Al4C3), the metallic atom wherein discharged or ion, non-metallic atom or ion, it it is all the ultra-fine fine particle of secondary nanophase, there is the specific surface area of maximum, be provided that the abundant disturbance in melt superfinishing microcell and activation effect, reach to expedite the emergence of critical nucleus and generate in a large number and the mechanism of inhibiting grain growth effect.By this mechanism, making matrix crystalline state generally become equiax crystal, grain size is averagely less than 120 μm, and further effect of optimization can reach grain size averagely in 50～100 μm.This effect, is to use merely the gas purification technique of the conventional die fining agent such as aluminum titanium boron and aluminum titanium carbon and routine to realize.
When the external Lewis Acids and Bases added in melt is to when decomposing, the intermetallic compound presoma that can differ from matrix Presence of an interface is the most also disturbed and activates and recurring structure fluctuating, produce more critical nucleus, make (T+ θ H) combination concentration mutually the most in the alloy and be evenly distributed density, make up to 1/[μm]2Above, here it is Lewis Acids and Bases can increase Subnano-class particle (T+ θ H) combination phase and nanoscale particle GP district, θ ＂, the mechanism of θ ＇ tandem reinforcement phase to disturbance and the activation effect at nanoscale.
To sum up, Lewis Acids and Bases pair of the present invention, variform can be shown as, the one in the positive and negative ion body being combined into including metal and part, complicated ligand compound, super large heteropoly compound, metal halogen compound, main group dvielement, interior transition dvielement, or more than one mixing.
Additionally, due to foreign peoples's material concentration that Lewis Acids and Bases is bigger to being supplied to alloy melt, therefore the constitutional supercooling degree of melt crystallization process is increased, nucleus is caused quickly to cross critical dimension under higher crystallization power, and free nucleation and growth in supercool liquid, formed and there is isotropism and shape closer to spherical equi-axed crystal；Therefore avoid or alleviate the component segregation of alloy, crystallize thick unidirectional, defect that macro property is uneven, thus it is prevented effectively from or alleviates some common deficiencies of alloy, such as pin hole, pore, shrinkage cavity and porosity, segregation, thick solid solution, high hardness compound, crackle etc..
The present invention is based on to the contrast image of alloy microstructure very high resolution and the structural analysis of precise and tiny constituency, it was found that intracrystalline also exists the hyperfine structure of (T+ θ H) excellent forked combination phase of sub-micron grade.Binary-phase each with Al-Cu compares, and (T+ θ H) combination has many advantages mutually, including: particle size is big, and anti-dislocation movement by slip face is big；Trunk portion T is the bar-shaped twin of high hard high stable compound polymerization, it is possible to walks around mode with dislocation and provides strength support for alloy；Its secondary θ H attachment on trunk oblique or be perpendicular to T mandrel direction and to surrounding matrix grows while with matrix coherence, enhance trunk and lattice dot matrix around is tightened up ability, or in other words, T mandrel is by adhering on it to the secondary phase of θ H of surrounding growth, tightening up the transmission of effect peripherad matrix space and diffusion, this effect, in secondary um region, matrix is created steel grid invigoration effect (can be described as " class concrete reinforced structure ") in concrete in similar building structure, makes matrix strength be greatly improved.This effect, if compared from monomer, be in matrix flake Al-Cu metastable phase (GP district, θ ＂, θ ＇ or other disc phase) or a combination thereof all far from comparing；But, in common aluminum bronze manganese systems (Al-Cu-Mn) alloy, owing to each binary Al-Cu metastable phase is in the distribution density of distribution density significantly larger than (T+ θ H) combination phase of intrinsic silicon, the effect of (T+ θ H) combination phase is caused to be blanked and be never found.
(T+ θ H) combination mutually in θ H but with not coordination to much bigger thickness (about 20nm), alloy substrate is created the strengthening contribution of the binary Al-Cu metastable phase being better than GP district, θ ＂, θ ＇ or other disc shaped with free state existence: θ H is except transmitting the peripherad matrix space of effect of tightening up of trunk T-phase and in addition to diffusion, owing to anti-matrix slide surface is bigger, thus bigger to matrix potentiation；Owing to direction is more, therefore isotropic uniformity is showed in the invigoration effect to matrix；Owing to being not belonging to high rigid particle, so still mode can be cut through with dislocation be supplied to the preferable plasticity and toughness of matrix；In a word, (T+ θ H) combination optimizes the thing phase molecule combinative structure of aluminum bronze manganese systems (Al-Cu-Mn) alloy mutually, provides walking around strengthening effect and cutting through strengthening effect two kinds effect higher than what free state Al-Cu metastable phase combined of high Hard Inclusion T-phase for matrix；So, research plays the comprehensive effect of this excellence, it is necessary to the combination of Al-Cu metastable phase is transferred out merely by the emphasis that design of material is paid close attention to from tradition, and concentrates on and expedite the emergence of (T+ θ H) combination phase in effect.
Inventive formulation is configured as one of technical way, is that the crystalline state combination making alloy realizes under the equiax crystal premise of mean grain size ＜ 120 microns, also can realize alloy grain internal (T+ θ H) combination phase amount 1/[μm]2Above.Therefore, main constituent content is by weight percentage: nickel: 0.15%-0.18%, manganese Mn :≤2%, cadmium Cd:0.05%～0.5%, copper Cu:4.2%～8.0% and Cu >=0.8Mn+4.05% or copper 0.5%≤Cu≤3% and Cu >=1.5Mn；Lewis Acids and Bases, to total amount 1% × 10-4～2.0% or 7.0%～9.0%, makes alloy mean grain size ＜ 120 microns, and surplus is aluminum Al.Improve elevated temperature strength and volume, the dimensional stability of alloy by adding nickel, and have the compound making Fe to become the tendency of bulk, reduce the illeffects of impurity F e, provide material base for mechanical index.
Detailed description of the invention
The specific embodiment of the invention includes 2 parts, and Part I is prompting and explanation, and Part II is specific embodiment.
Part I: point out and illustrate
A kind of preparation method substituting the blue aluminum alloy materials of QT500 high pressure method, comprises the steps of
(1) in the range of aforementioned Lewis Acids and Bases is to, element ratio, selected one group of combinations of substances, determine weight ratio, the alloy total amount prepared as required, extrapolate the weight of every kind of required material；
(2) adding aluminium ingot or molten aluminum liquid in smelting furnace, heating is also incubated more than 700 DEG C；
(3) addition manganese Mn, cadmium Cd, copper Cu, nickel stirs, and adds selected Lewis Acids and Bases pair, or the Lewis Acids and Bases that addition is selected is to combination, stirs；
(4) then above-mentioned alloy melt is carried out furnace refining；
(5) remove the gred after refine, stand, sample analysis alloy composition, adjust chemical composition in the deviation range of regulation according to analysis result；Homoiothermic is to more than 650 DEG C, and aluminium alloy is come out of the stove, online degasification, slagging-off；
(6) casting: use gravity casting and pouring.
Described gravitational casting, step is as follows:
1. pourable casting after melt filtration, casting temperature controls can be at 700～730 DEG C；
2. mould should be preheating to about 450 DEG C before casting, install core, by compressed air, mold cavity is blown clean, prevent field trash from entering alloy and cause waste product；
3. complete on convertible gravity casting machine, can take manually to pour into a mould or automatization's cast, closed die also makes casting machine be turned to certain angle, in stove, dip appropriate aluminium alloy with casting ladle and pour in mould switching bag, casting machine is made slowly to be turned to horizontal level, in switching process, aluminium alloy is full of die cavity from switching bag by ingate；Natural cooling or the coldest；
4. product, natural cooling, cleaning core, sawing rising head, polishing overlap are taken out in die sinking；
5. appearance quality detection.Rough casting, before carrying out presentation quality inspection, should be cleaned out smooth, and the dead head of non-machined surface should be cleaned to cast(ing) surface and flush；
6. internal soundness detection.Section dye penetrant inspection detection or integral fluorescence or X-ray check；
7. solution treatment.Solid solution furnace sent into by the blank that foundry goods completes roughing and inside and outside quality testing, carries out the solution treatment of less than 560 DEG C, quenches at once after insulation, and water-cooled or oil are cold；
8. ageing strengthening.The foundry goods completing solution treatment is sent into aging furnace and carries out ageing strengthening process, ageing strengthening technique 150～240 DEG C, after insulation, natural cooling of coming out of the stove；Cast(ing) surface can carry out impeller blasting.
9. sample analysis test checking.
Part II: specific embodiment
Embodiment 1
1、A kind of aluminium alloy high pressure square flange substituting QT500Composition by weight percent is: nickel: 0.15%, copper Cu:6.6%, manganese Mn:0.6%, cadmium Cd:0.05%, chromium Cr:0.3%, bismuth Bi:0.1%, lanthanum La:0.03%, four cyano cadmium anion body [Cd (CN)4]2 -: 0.03%, hexafluoro closes potassium silicate K2[SiF6]: 0.04%, CuCl3: 0.04%；
2, preparation method: melting → degasification → cast → cooling → die sinking pickup → cleaning, sawing → solid solution → timeliness；
3, melt cast temperature >=680 DEG C；
4, mold preheating temperature >=300 DEG C；
5, filling time >=5s；
6, cool time: >=60s pressurising time；
7, heat treatment: T6 solid solution adds complete artificial aging；
8, cast microstructure index: metallographic structure is equiax crystal, mean grain size 80 ~ 110 μm, (T+ θ H) combination phase amount 2 ~ 3/[μm] in crystal grain2；
9, foundry goods mechanical performance
| Power resistance strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 536 | 455 | 159 | 5.4 |
Embodiment 2
1、A kind of aluminium alloy high pressure square flange substituting QT500Composition by weight percent is: nickel: 0.16%, copper Cu:6.7%, manganese Mn:0.7%, cadmium Cd:0.05%, chromium Cr:0.35%, bismuth Bi:0.1%, lanthanum La:0.03%, four cyano cadmium anion body [Cd (CN)4]2 -: 0.03%, hexafluoro closes potassium silicate K2[SiF6]: 0.04%, CuCl3: 0.04%；
2, concrete preparation method is same as in Example 1；
3, cast microstructure index: metallographic structure is equiax crystal, mean grain size 80 ~ 120 μm, (T+ θ H) combination phase amount 2 ~ 3/[μm] in crystal grain2；
4, foundry goods mechanical performance
| Power resistance strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 550 | 460 | 160 | 5.6 |
Embodiment 3
1、A kind of aluminium alloy high pressure square flange substituting QT500Composition by weight percent is: nickel: 0.18%, copper Cu:7.1%, manganese Mn:0.7%, cadmium Cd:0.05%, four cyano cadmium anion body [Cd (CN)4]2 -: 0.03%；
2, concrete preparation method is same as in Example 1；
3, cast microstructure index: metallographic structure is equiax crystal, mean grain size 80 ~ 120 μm, (T+ θ H) combination phase amount 2/[μm] in crystal grain2；
4, foundry goods mechanical performance
| Power resistance strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 535 | 450 | 149 | 5.6 |
Claims (9)
1. one kind substitutes the aluminum alloy materials that QT500 high pressure method is blue, it is characterized in that: main constituent content by weight percentage: nickel: 0.15%-0.18%, manganese Mn :≤2%, cadmium Cd:0.05%～0.5%, copper Cu:4.2%～8.0% and Cu >=0.8Mn+4.05% or copper 0.5%≤Cu≤3% and Cu >=1.5Mn；Lewis Acids and Bases, to total amount 1% × 10-4～2.0% or 7.0%～9.0%, makes alloy mean grain size ＜ 120 microns, and surplus is aluminum Al.
A kind of aluminum alloy materials substituting QT500 high pressure method orchid the most according to claim 1, it is characterised in that: alloy grain is equiax crystal.
A kind of aluminum alloy materials substituting QT500 high pressure method orchid the most according to claim 1, it is characterised in that: in alloy grain, sub-nanometer (T+ θ H) combination phase amount reaches >=1/square micron.
A kind of aluminum alloy materials substituting QT500 high pressure method orchid the most according to claim 1, it is characterized in that: the one in the described Lewis Acids and Bases positive and negative ion body to being combined into for metal and part, complicated ligand compound, super large heteropoly compound, metal halogen compound, main group dvielement, interior transition dvielement, or more than one mixing.
A kind of aluminum alloy materials substituting QT500 high pressure method orchid the most according to claim 4, it is characterised in that: cation body, anion body that described metal and part are combined into comprise four cyano cadmium anion body [Cd (CN)4]2 -。
A kind of aluminum alloy materials substituting QT500 high pressure method orchid the most according to claim 4, it is characterised in that: described complicated ligand compound or super large heteropoly compound comprise hexafluoro and close potassium silicate K2[SiF6]。
7. according to a kind of aluminum alloy materials substituting QT500 high pressure method orchid one of claim 1-6 Suo Shu, it is characterized in that: described Lewis Acids and Bases pair, Al matrix percentage by weight is accounted for by element addition, scope is: Cr ＜ 0.5%, Bi ＜ 0.1%, La ＜ 0.03%, K2[SiF6] ＜ 0.04%, CuCl3＜ 0.04%, [Cd (CN)4]2 -＜ 0.04%.
A kind of preparation method substituting the blue aluminum alloy materials of QT500 high pressure method the most as claimed in claim 7, it is characterised in that: comprise the steps of
(1) in the range of aforementioned Lewis Acids and Bases is to, element ratio, selected one group of combinations of substances, determine weight ratio, the alloy total amount prepared as required, extrapolate the weight of every kind of required material；
(2) adding aluminium ingot or molten aluminum liquid in smelting furnace, heating is also incubated more than 700 DEG C；
(3) addition manganese Mn, cadmium Cd, copper Cu, nickel stirs, and adds selected Lewis Acids and Bases pair, or the Lewis Acids and Bases that addition is selected is to combination, stirs；
(4) then above-mentioned alloy melt is carried out furnace refining；
(5) remove the gred after refine, stand, sample analysis alloy composition, adjust chemical composition in the deviation range of regulation according to analysis result；Homoiothermic is to more than 650 DEG C, and aluminium alloy is come out of the stove, online degasification, slagging-off；
(6) casting: use gravity casting and pouring.
A kind of preparation method substituting the blue aluminum alloy materials of QT500 high pressure method the most according to claim 8, it is characterised in that: described gravity casting and pouring, step is as follows:
1. pourable casting after filtering；
2. mould should be preheated before casting, install core, by compressed air, mold cavity is blown clean；
3. take manually to pour into a mould or automatization's cast, in stove, dip aluminium alloy with casting ladle and pour mould gate into and be full of die cavity by ingate；Natural cooling or the coldest；
4. product, natural cooling, cleaning core, sawing rising head, polishing overlap are taken out in die sinking；
5. appearance quality detection: rough casting, before carrying out presentation quality inspection, should be cleaned out smooth, the dead head of non-machined surface should be cleaned to cast(ing) surface and flush；
6. internal soundness detection；
7. solution treatment: solid solution furnace sent into by the blank that foundry goods completes roughing and inside and outside quality testing, carries out less than 560 DEG C solution treatment, quenches at once after being incubated, uses water-cooled or oil cold；
8. ageing strengthening: the foundry goods completing solution treatment is sent into aging furnace and carries out ageing strengthening process, ageing strengthening below 230 DEG C, after insulation, natural cooling of coming out of the stove；
9. sample analysis test checking；
10. Practical Performance checking.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610493119.6A CN105937004B (en) | 2016-06-29 | 2016-06-29 | A kind of aluminum alloy materials and its gravity casting method substituting QT500 high pressure method orchids |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610493119.6A CN105937004B (en) | 2016-06-29 | 2016-06-29 | A kind of aluminum alloy materials and its gravity casting method substituting QT500 high pressure method orchids |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105937004A true CN105937004A (en) | 2016-09-14 |
| CN105937004B CN105937004B (en) | 2018-09-07 |
Family
ID=56872914
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610493119.6A Active CN105937004B (en) | 2016-06-29 | 2016-06-29 | A kind of aluminum alloy materials and its gravity casting method substituting QT500 high pressure method orchids |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105937004B (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101850856A (en) * | 2010-05-15 | 2010-10-06 | 中山市华明泰化工材料科技有限公司 | Compression type quantitative packing machine of super micropowder light powder and packing method thereof |
| CN102828088A (en) * | 2011-06-14 | 2012-12-19 | 湖南晟通科技集团有限公司 | Cu-Mn high-strength heatproof aluminium alloy material |
| CN103131919A (en) * | 2011-11-29 | 2013-06-05 | 贵州科学院 | High-strength aluminum alloy material formed through metamorphism of salt hexafluorosilicate |
| CN103334034A (en) * | 2013-06-14 | 2013-10-02 | 宁波科达制动器制造有限公司 | Preparation method of gas compressor volute of turbocharger |
-
2016
- 2016-06-29 CN CN201610493119.6A patent/CN105937004B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101850856A (en) * | 2010-05-15 | 2010-10-06 | 中山市华明泰化工材料科技有限公司 | Compression type quantitative packing machine of super micropowder light powder and packing method thereof |
| CN102828088A (en) * | 2011-06-14 | 2012-12-19 | 湖南晟通科技集团有限公司 | Cu-Mn high-strength heatproof aluminium alloy material |
| CN103131919A (en) * | 2011-11-29 | 2013-06-05 | 贵州科学院 | High-strength aluminum alloy material formed through metamorphism of salt hexafluorosilicate |
| CN103334034A (en) * | 2013-06-14 | 2013-10-02 | 宁波科达制动器制造有限公司 | Preparation method of gas compressor volute of turbocharger |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105937004B (en) | 2018-09-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105970010B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT400 light-duty vehicle steering gears | |
| CN105936999A (en) | Aluminum alloy material replacing QT450 half pipe and gravity casting method of aluminum alloy material | |
| CN105937000B (en) | A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns | |
| CN105970047A (en) | Aluminum alloy material for replacing QT500 agricultural machinery speed reducer and investment casting method thereof | |
| CN105937002B (en) | A kind of aluminum alloy materials and its injection molding method substituting QT600 rolls | |
| CN106119634B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT500 filters | |
| CN105936995A (en) | Aluminum alloy material replacing QT400 automobile control arm and semi-solid state die-casting forming method of aluminum alloy material | |
| CN105970041B (en) | A kind of aluminum alloy materials and its centre spinning method of replacement QT500 looms pump connecting seat | |
| CN105936998B (en) | A kind of replacement aluminum alloy materials of QT450 automobile turbocharger housings and its sand casting forming method | |
| CN105970052B (en) | A kind of aluminum alloy materials and its sand mould casting method for substituting QT500 heavy type car steering gears | |
| CN105936997B (en) | A kind of aluminum alloy materials and its pressure casting forming method for substituting QT500 automobile axle housings | |
| CN105937004A (en) | Aluminum alloy material replacing QT500 high-pressure square flange and gravity casting method of aluminum alloy material | |
| CN105970039B (en) | A kind of aluminum alloy materials and its centre spinning method for substituting QT500 loom wheel hubs | |
| CN105970055B (en) | A kind of aluminum alloy materials and its centre spinning method substituting QT450 air caps | |
| CN106065446B (en) | A kind of aluminum alloy materials and its sand mould casting method substituting QT400 well lids | |
| CN105970054A (en) | Aluminum alloy material for replacing QT450 vacuum single-chip hoop and sand model casting method thereof | |
| CN105970043B (en) | A kind of aluminum alloy materials and its high-pressure casting method of replacement QT500 Flange filters | |
| CN105970045B (en) | The aluminum alloy materials and its gravity casting method of a kind of elastic seat sealed first valves of replacement QT400 | |
| CN105936996B (en) | A kind of aluminum alloy materials and its liquid forging forming method substituting QT500 automotive hub | |
| CN105970048B (en) | A kind of replacement aluminum alloy materials of the full hydrostatic drives of QT500 agricultural machinery and its liquid forging casting method | |
| CN105970042A (en) | Aluminum alloy material for replacing QT450 loom balance block and metal gravity casting method thereof | |
| CN105970049B (en) | A kind of aluminum alloy materials and its high-pressure casting method substituting QT500 crampons | |
| CN105970050B (en) | A kind of aluminium alloy crane arm material and its sand mould casting method for substituting QT500 | |
| CN105970046B (en) | A kind of aluminum alloy materials and its low-pressure casting method substituting QT500 agricultural machinery hydraulic pumps | |
| CN105970051B (en) | A kind of aluminum alloy materials and its sand mould casting method substituting the high-power truck steering gears of QT600 |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |