CN105970040A - Aluminum alloy material substituting for QT500 picking disc and centrifugal casting method of aluminum alloy material - Google Patents
Aluminum alloy material substituting for QT500 picking disc and centrifugal casting method of aluminum alloy material Download PDFInfo
- Publication number
- CN105970040A CN105970040A CN201610489541.4A CN201610489541A CN105970040A CN 105970040 A CN105970040 A CN 105970040A CN 201610489541 A CN201610489541 A CN 201610489541A CN 105970040 A CN105970040 A CN 105970040A
- Authority
- CN
- China
- Prior art keywords
- aluminum alloy
- alloy
- dish
- spear
- casting
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D13/00—Centrifugal casting; Casting by using centrifugal force
-
- 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
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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 substituting for a QT500 picking disc and a centrifugal casting method of the aluminum alloy material. The aluminum alloy material is characterized by comprising the following main components in percentage by weight: 0.005% to 0.02% of Co, not more than 2% of Mn, 0.05% to 0.5% of Cd, 4.2% to 8.0% of Cu, 1%*10<-2> to 2.0% of one or more Lewis acid-base pairs, and the balance of Al, wherein the following formula is met: Cu is greater than or equal to 0.8*Mn + 4.05%; and as the total amount of the Lewis acid-base pairs is 1%*10<-2> to 2.0%, the mean grain size of the aluminum alloy material is smaller than 120 micrometers.
Description
Technical field
The present invention relates to a kind of QT500 of replacement throw a spear the aluminum alloy materials and preparation method thereof of dish.
Background technology
Spheroidal graphite cast-iron (abbreviation magnesium iron) is one of primary base material in steel industry, is extensively heavily used for system
Making stress complicated, intensity, toughness, wearability etc. require higher part, such as universal machine, lifting, agricultural, automobile, cast, spin
Knit, 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
The connection of hub, shaft member, ball, driving member, suspender, hook fastener, conducting element, tumbler etc.；
Magnesium iron is the most of many uses, and also residing in it has the standard brand of segmentation, and every kind of trade mark defines more strict accurate
Chemical composition combination, specification of heat treatment parameter, mechanical property and physical index etc., thus correspond to segmentation application category.See
Table 1.
Mechanical property that the spheroidal graphite cast-iron trade mark that table 1 GB/T 1348 determines is corresponding and tissue
This mechanical performance index of magnesium iron and criteria for classification thereof, can as aluminum alloy materials innovative design, carry high performance
To mark basis, can simultaneously serve as the comparison passage of " with aluminum for steel ", it may be assumed that if aluminium alloy can substitute certain trade mark magnesium iron, then
Substitute the steel close with this trade mark performance further, just be enough to lead a kind of trend or fashion in industrial circle.
From the perspective of natural characteristic and experience accumulation, aluminum and aluminium alloy have a multiple advantage compared with magnesium iron:
1. aluminum has fabulous cryogenic property, and its mechanical property reduces with temperature and improves, at cold season and low temperature ring
Border has unique advantage as structural material, and magnesium iron then reduces with temperature and gradually occurs by toughness to the transformation of fragility, especially
Below brittle transition temperature, its impact value drastically declines, and even " low-temperature brittle fracture " occurs.
2. aluminum and aluminium alloy specific strength are high, have good fracture toughness, and magnesium iron improves and elongation percentage with yield strength
Declining, the sensitivity that counter stress is concentrated substantially increases, and after showing as surrendering, deflection is less i.e. ruptures, this " fatigue clear break "
Person's character is often the civil infrastructure potential hard defects without sign overall collapse formula destruction suddenly, is many great serious accidents
Arch-criminal.
3. owing to aluminum and aluminium alloy are compared with the thermal capacitance of magnesium iron and steel is big and heat conductivity is good, thus its prevent fires, explosion-proof, early warning more
Good.
4. the antioxidant anticorrosive of aluminum and aluminium alloy itself significantly larger than iron and steel and being more suitable for carries out high-tech surface and prevents
Rotten and decoration integrated process.
5. aluminum alloying and Technology for Heating Processing relatively magnesium iron is simple, and the alloying temperature of aluminum is generally below 750 DEG C, at heat
Reason temperature, between 150～600 DEG C, is divided by effect and also only has solid solution, timeliness, several simple process of homogenizing annealing, and ball
The alloying temperature of ferrum is more than 1400 DEG C, and heat treatment temperature then at 500～1000 DEG C, is divided into Stress relieving annealing, height by effect
The series of complex technique such as temperature graphitizing annealing, normalizing, quenching and tempering, many temperature quenching, surface hardening, thermo-chemical treatment, no
But process is complicated, equipment technology requires height, and consuming and discharging also is aluminum several times or even more than ten times.
Compare from machinery (pressure) processing technique and equipment, aluminum can use easily casting, roll, squeeze, forge,
The techniques such as saw, milling, weldering, punching press, and magnesium iron can not extrusion process, other processing method is also required to use the ratio specification of aluminum
The process equipment much bigger with power and frock, to the manufacturing process of finished parts, almost every one procedure link magnesium iron and steel
Will consume more higher power than aluminum.
7. along the whole life cycle of parts application, magnesium iron lacks because of big, heavy, perishable, the easy brittle failure of its inertia etc.
Falling into, its material consumption, energy consumption and maintenance cost are significantly larger than aluminum, and its value recycled is also far below aluminum.
These steel aforementioned shortcoming and the unique superior quality of aluminum, the marked improvement for " with aluminum for steel " provides
The basis of reality that civilization of human society progress is pursued.
In the technology upgrading of " with aluminum for steel ", in order to give full play to aluminium alloy with " gently " the superior spy of series as representative
Property, it is necessary to 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 combined by the functional microcosmic thing that carry this feature
Contribute out, therefore obtain good functional thing combined, such as high intensity, high-melting-point, high-ductility, high rigidity, corrosion resistant
Erosions etc., are the final results of various preparation method pursuit, thus, the Design of Chemical Composition of aluminium alloy also exists with its technology of preparing
Closely internal integrity, this uniformity, in short, be a kind of atom pass of how being combined into required " thing phase molecule "
System, the i.e. thing of material can regard a kind of molecular structure mutually as.The mixed smelting of formula element and casting crystalline, be fusion casting shape
Become the major contributing link of material thing phase molecule combinative structure, in fusion-casting process, between the metal of solid solution crystal grain and crystal boundary
Compound molecule thing determines crystalline state combination (submicron particles: about yardstick 10～300 μm) of alloy, subsequent heat treatment mutually
Or flow harden is then to fine structure under crystalline state group frame (micron particles: about yardstick 1～30 μm) or even more
The precise and tiny structure (Subnano-class or sub-micron grade particle: yardstick 10nm～＜ 1 μm) of microcosmic is adjusted and perfect, this adjustment
With perfect degree and scope, in known technology and traditional view, it is believed that main by the alloy phase residing for alloy composition
The combined decision of thing that graph region is given, but, alloy phase diagram does not provide the interpolation of other trace element and gets rid of generation
Impact, adds with less prediction and gets rid of the directiveness that thing is affected by other trace element mutually.Use for reference alloy solution chemistry
Theoretical and method improves melt structure, the covering of such as protecting film, the interpolation of slag former, refining agent or alterant, and degasification removes the gred
Purify, be 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 " become
Set up meter separately " part.
On engineer applied, the size of aluminum alloy solution body crystal grain and state, and it is distributed in the intermetallic of crystal boundary
The size and form of thing, has conclusive impact to the mechanical property of alloy.Thick plane crystalline substance, dendrite, column crystal etc. are no
Ordered crystal and the thick brittle property intermetallic compound being distributed in crystal boundary, it is possible to the fine structure that alloy is good and precise and tiny knot
The obdurability of matrix is contributed and is all balanced out, because the law of development that these coarse grains are deferred to results from casting mold cavity by structure
The raw core of type wall, from the unidirectionally extended growth pattern of export-oriented liquid internal, cause alloy component segregation, crystallize thick unidirectional,
The defect that macro property is uneven, thus become some common deficiencies of alloy, such as pin hole, pore, shrinkage cavity and porosity, segregation, thick
The root of big solid solution, high hardness compound, crackle etc..The routine used at present goes bad the means of means and crystal grain thinning, as
Adding aluminum titanium boron or Al-Ti-C master alloy, best effect can only make mean grain size refine to 120～150 microns, and branch
Brilliant form does not often have basic transformation, and this is the important bottleneck problem that alloy mechanical property improves.Because aluminum is closed
For gold, it is thus achieved that the refinement of the approach that intensity and toughness improve simultaneously, only crystal grain and rounding；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, the thinnest
Change 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
Bulky grain has the highest titanium Ti and rare earth concentration, and as the material for promoting crystal grain to refine, this phenomenon shows Ti and rare earth
Move towards to need the opposite of solution problem；And in the production process of 211Z alloy-steel casting, also occur and common aluminum alloy
The most common defect, 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
Study, especially the formation mechenism of thing phase molecule combinative structure is furtherd investigate, just can see clearly essence, and then find solution
Certainly problem, the effective way of elimination defect.
Scan thoroughly by aluminum bronze manganese systems (Al-Cu-Mn) alloy being up to the spherical aberration correction of the very high resolution of 0.08nm
Penetrate ultramicroscope (STEM) precise and tiny constituency to analyze, it is thus achieved that set up various phase structures on an atomic scale, Atomic Resolution
It is distributed with chemical element.Confirm wherein 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) group
Closing phase, the trunk portion T-phase of this combination phase is Al-Cu-Mn ternary phase, molecular structural formula Al20Cu2Mn3, molecule phase character is
Diameter about 100nm, length about 600～1000nm are { the 010} face coherence in mandrel shape and its (010) face and alloy matrix aluminum；And T
Mutually around apposition growth size is compared with the secondary phase of Al-Cu binary of big (thickness about 20nm, be about 50nm), due to this secondary phase with
In matrix, other Al-Cu metastable phase (GP district, θ ＂, θ ＇ or other disc phase) compares, and structurally has very big difference, particularly
Thickness is thicker much than other Al-Cu metastable phase, and therefore the present invention is referred to as θ H phase, its molecular structural formula Alx(x is likely less than Cu
2), it 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
, hinder the strongest, the intensity of material is the biggest.And particle hinders the knot that behavior interacts with material median surface or dislocation movement by slip
Really, having two kinds: one is when the strong hardness of particle own is not high enough, dislocation will cut through particle and continue sliding, and another kind is particle
Intensity is the highest, and dislocation cannot cut through, then can only walk around particle and continue sliding, and leave a circle dislocation ring around particle.
The size that the strength of materials is contributed by two kinds of results is apparent from: walks around particle ratio and cuts through particle to the strength of materials
Contribution big；Cutting through particle can provide material preferable elongation percentage, and walks around particle due to the potentiation of dislocation ring, will carry
For the higher yield strength of material and tensile strength.
In the traditional view about aluminum bronze manganese systems (Al-Cu-Mn) alloy, owing to the most all thinking that Al-Cu Binary-phase is
The principal element of alloy strengthening, therefore, the emphasis that investigation of materials and design are paid close attention to, it is simply that make each metastable state of Al-Cu Binary-phase real
Best of breed the most in the alloy.Though it has also been found that there is T ternary phase, be not to be considered as T-phase can be with to the contribution of alloy strength
The combination of each metastable phase of Al-Cu binary is compared, and thinks that T-phase is easily assembled at crystal boundary and form thick brittlement phase, therefore wants tight
Lattice control its quantity.
The binary Al-Cu metastable phase of GP district, θ ＂, θ ＇ or other disc shaped belongs to dislocation to the contribution feature of alloy strength
Cutting through particle mode, be characterized in that disc looks the biggest, cut through the most difficult, therefore the contribution to intensity is the biggest, but, work as dish
Sheet is big to a certain extent (more than 150nm, thickness only has 1～3nm to diameter), its lattice dot matrix and the mismatch of matrix lattice dot matrix
Spend height, the most no longer can keep complete coherence with matrix, and gradually show the feature of brittlement phase.Therefore, coherence should be kept again
The mismatch stress field having maximum hinders dislocation movement by slip ability to play maximum, and binary Al-Cu each metastable phase particle has one most preferably
The problem of combination, is also required to it simultaneously and the elongation percentage of matrix keeps bigger contribution, before this is or even from now on design of material
One of subject matter to be considered.
As it was previously stated, the dish of throwing a spear that tradition magnesium iron (QT500) makes, during actual manufacture, use below existence
Defect:
1. relatively low because of magnesium iron elongation percentage, the sensitivity that counter stress is concentrated substantially increases, and deforms after showing as surrendering
Measure less easy fracture, cause the accident.
2. magnesium iron heat treatment process is complicated, equipment technology requirement is high, and consumes and discharge the biggest.
3. along the whole life cycle of parts application, magnesium iron lacks because of big, heavy, perishable, the easy brittle failure of its inertia etc.
Falling into, its material consumption, energy consumption and maintenance cost are higher than very much, and its value recycled is relatively low.
Aluminium alloy makes loom dish of throwing a spear and has no correlational study at home, because the limitation of common aluminum alloy basic material
Property, its mechanical property is relatively low, especially high-temperature heat-resistance performance, and the temperature born is less than 300 DEG C, has had a strong impact on the longevity of dish of throwing a spear
Life, even adds security risk.
Summary of the invention
The technical problem to be solved in the present invention is: provide aluminum alloy materials and preparation thereof that a kind of QT500 of replacement throws a spear dish
Method, wherein adds Lewis Acids and Bases pair, effectively to expedite the emergence of critical nucleus (obtaining equiax crystal), makes alloy obtain before curing
The optimal combined structure of molecule thing ((T+ θ H) combines phase), promotes alloy crystalline state optimization, enables aluminum alloy to base material and realize 500MPa
And higher strength grade, thus reach to produce and substitute QT500 and throw a spear the Al-alloy products of dish.
The technical scheme is that a kind of QT500 of replacement throws a spear the aluminum alloy materials of dish, main constituent content by weight hundred
Proportion by subtraction meter: cobalt Co:0.005%-0.02%；Manganese Mn :≤2%, cadmium Cd:0.05%～0.5%, copper Cu:4.2%～8.0% and Cu >=
0.8Mn+4.05%；Lewis Acids and Bases is to total amount 1% × 10-2～2.0%, making alloy mean grain size ＜ 120 microns, surplus is aluminum
Al。
Described alloy grain is equiax crystal.
In described alloy grain, sub-nanometer (T+ θ H) combination phase amount reaches >=5/square micron.
Described Lewis Acids and Bases to for the one in the carbide of metal, main group dvielement, interior transition dvielement, or one
Plant mixed above.
The carbide of described metal, including zirconium carbide ZrC.
Described Lewis Acids and Bases pair, accounts for Al matrix percentage by weight by element addition, and scope is: Ti ＜ 0.05%, Y ＜
0.04%, Nd ＜ 0.13%, Mg ＜ 0.4%, ZrC ＜ 0.06%.
A kind of QT500 of replacement throws a spear the preparation method of aluminum alloy materials of dish, 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, as required
The alloy total amount of preparation, extrapolates 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) manganese Mn, cadmium Cd, copper Cu, cobalt Co are added, stirring, add selected Lewis Acids and Bases pair, or add selected Louis
This acid-base pair combines, and 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 to regulation according to analysis result
In deviation range；Homoiothermic is to more than 650 DEG C, and aluminium alloy is come out of the stove, online degasification, slagging-off；
(6) casting: use centrifugal casting cast.
Described centrifugal casting is poured into a mould, and step is as follows:
(1) melt proceeds to casting ladle from holding furnace；
(2) casting mold is preheating to preference temperature；
(3) open driving motor, band movable belt pulley and wheel shaft to rotate, and then drive the casting mold being mounted on an axle to rotate；
(4) adjustment casting mold rotating speed is 50～1500r/min, and the casting ladle that verts makes melt flow into running gate system along pouring basin, passes through
Running gate system flows into casting mold, is full of casting mold die cavity under casting mold rotary centrifugal force effect；
(5), after melt solidifies completely, stop the rotation, die sinking pickup；
(6) product, natural cooling, cleaning core, sawing rising head, polishing overlap are taken out in die sinking；
(7) appearance quality detection: rough casting, before carrying out presentation quality inspection, should be cleaned out smooth, non-machined surface
Dead head should be cleaned to cast(ing) surface and flush；
(8) internal soundness detection；
(9) 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 after being incubated at once, uses water-cooled or oil cold；
(10) ageing strengthening: the foundry goods completing solution treatment is sent into aging furnace and carries out ageing strengthening process, time below 230 DEG C
Effect strengthening, after insulation, natural cooling of coming out of the stove；
(11) sample analysis test checking；
(12) Practical Performance checking.
Beneficial effects of the present invention: pointed by lewis' theory of acids and bases, molecule solution can occur in aluminium alloy melt
Body or " acid-base pair " material of (i.e. less than the scope of 1 nanometer) thing phase molecule structure optimization, application in contributing to time nano-area
Fine structure in 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, with (0.1nm～10nm yardstick model in providing the hyperfine microcell of melt
Enclose) abundant disturbance and activation effect, reach to expedite the emergence of critical nucleus and formed in a large number, make alloy grain degree be refined further,
Form more rounding；Optimize very small areas (micron order: about yardstick 1～30 μm) and precise and tiny region (Subnano-class or secondary simultaneously
Micron order particle: yardstick 10nm～＜ 1 μm) thing phase molecule combinative structure, increase (T+ θ H) combine in alloy substrate
Content, is the mechanism problem of the alloy strengthening that the present invention solves.
Due to the discovery of (T+ θ H) combination phase, when aluminium alloy strengthening design, it is possible to by increasing (T+ θ H) combination phase,
The matrix strength enabling aluminum alloy to material obtains big lifting, is well controlled between 400～600MPa in yield strength, this
It is the engineer applied problem that the invention solves the problems that, i.e. alternate series ductile iron material and goods.
For aluminium alloy melt, the boride of metal such as molybdenum boride MoB (or MoB2), the carbide such as titanium carbide of metal
TiC, the nitride such as tungsten nitride WN of metal2, or the complex chemical compound such as boron carbide B of the boron carbon nitrogen of metal4C, aluminum titanium nitrogen
AlTiN or aluminum chromium nitrogen AlCrN, combines with covalent bond between its atom, has the feature of Lewis Acids and Bases pair, and these are in normal conditions
The particularly preferred material of sufficiently stable and thermostability, after blowing into melt dispersedly with nanomorphic powder, due to high temperature, rich electricity
Sub and the biggest specific surface area, the interface energy of generation be enough to cause material molecule to occur polarization deformation or even disproportionation to decompose, also
Disturbance and activation effect can be caused in nanometer range, therefore, the boride of metal, the carbide of metal, the nitride of metal or
The complex chemical compound of the boron carbon nitrogen of person's metal, it is also possible to be attributed to " Lewis Acids and Bases to ".
To sum up, Lewis Acids and Bases pair of the present invention, variform can be shown as, including boride, the metal of metal
The complex chemical compound of boron carbon nitrogen of carbide, the nitride of metal or metal, main group dvielement, transition group dvielement, interior
One in transition dvielement, or more than one mixing.
Further, since foreign peoples's material concentration that Lewis Acids and Bases is bigger to being supplied to alloy melt, therefore increase
The constitutional supercooling degree of melt crystallization process, causes nucleus quickly to cross critical dimension under higher crystallization power, and supercool
Free nucleation and growth in liquid, formed and have isotropism and shape closer to spherical equi-axed crystal；Due to equiax crystal
This because of the free growing endogenetic forming mechanism of liquid internal, change the irregular crystal edge such as plane crystalline substance, dendrite, column crystal
The growth pattern that the raw core of type wall in casting mold cavity, the most export-oriented liquid internal are unidirectionally extended, therefore avoids or alleviates alloy
Component segregation, crystallize thick unidirectional, defect that macro property is uneven, thus it is common to be prevented effectively from or alleviate some of alloy
Defect, 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, (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 that high hard high stable compound gathers
The bar-shaped twin closed, it is possible to walk around mode with dislocation and provide strength support for alloy；Its secondary θ H adheres on trunk
Oblique or be perpendicular to T mandrel direction and to surrounding matrix growth simultaneously with matrix coherence, enhance trunk to lattice-site around
The ability of tightening up of battle array, or in other words, T mandrel by adhering to it on to the secondary phase of θ H of surrounding growth, tighten up act on to
Matrix space transmission around and diffusion, this effect, create steel in similar building structure in secondary um region to matrix
Reinforced net invigoration effect in concrete, makes matrix strength be greatly improved.This effect, if compared from monomer, is matrix
Middle flake Al-Cu metastable phase (GP district, θ ＂, θ ＇ or other disc phase) or a combination thereof are all far from comparing；But,
In common aluminum bronze manganese systems (Al-Cu-Mn) alloy, due to each binary Al-Cu metastable phase intrinsic silicon distribution density far away
Higher than the distribution density of (T+ θ H) combination phase, 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, alloy substrate is created be better than with trip
The strengthening contribution of the binary Al-Cu metastable phase of GP district, θ ＂, θ ＇ or other disc shaped that amorph exists: θ H is except trunk T-phase
Effect of tightening up peripherad matrix space transmission and diffusion outside, owing to anti-matrix slide surface is bigger, therefore to matrix potentiation
Bigger；Owing to direction is more, therefore isotropic uniformity is showed in the invigoration effect to matrix；Owing to being not belonging to high rigid matter
Point, so still can cut through mode with dislocation to be supplied to the preferable plasticity and toughness of matrix；In a word, (T+ θ H) combination optimizes aluminum bronze manganese mutually
The thing phase molecule combinative structure of system's (Al-Cu-Mn) alloy, walks around strengthening effect and height for what matrix provided high Hard Inclusion T-phase
Strengthening effect two kinds effect is cut through in what free state Al-Cu metastable phase combined；So, research plays the comprehensive effect of this excellence
Should, 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 (T+ θ
H) combination the expediting the emergence of in effect of phase.
Inventive formulation is configured as one of technical way, is that the crystalline state combination making alloy realizes mean grain size ＜
Under the equiax crystal premise of 120 microns, also can realize alloy grain internal (T+ θ H) combination phase amount 5/[μm]2Above.Cause
This, main constituent content by weight percentage: cobalt Co:0.005%-0.02%；Manganese Mn :≤2%, cadmium Cd:0.05%～0.5%, copper
Cu:4.2%～8.0% and Cu >=0.8Mn+4.05%；Lewis Acids and Bases is to total amount 1% × 10-2～2.0%, make alloy mean grain size
＜ 120 microns, surplus is aluminum Al.Add transition group dvielement cobalt (Co) trace additives as complex alloys,
Alloy is formed AlCo, Al9Co2Deng 8 kinds of dispersivity High-Temperature Strengthening phases, Co is the high strength cast aluminum alloys of complex alloys
Trace additives, when it coexists with Mn, forms Al4Etc. (CoFeMn) the most complicated hardening constituent is in interdendritic, hinders dislocation, resistance
Only grain sliding, is effectively improved room temperature and high temperature (at the 400 DEG C) intensity of alloy.
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 for being embodied as
Example.
Part I: point out and illustrate
The step that alloy melt prepares:
1, in the range of aforementioned Lewis Acids and Bases is to, element ratio, selected one group of combinations of substances, determine weight ratio, as required
The alloy total amount of preparation, extrapolates the weight of every kind of required material, works out alloy production list of ingredients, and it is each to press list of ingredients choosing foot
Plant and get the raw materials ready.
2, adding appropriate aluminium ingot or molten aluminum liquid in smelting furnace, heating is allowed to melt completely and protect more than 700 DEG C
Temperature；For preventing melt from sucking too much air, fusion process should complete with in enclosed environment the most at short notice.
3, add manganese Mn, cadmium Cd, copper Cu, cobalt Co by formula proportion, after stirring, add selected Lewis Acids and Bases
Right, or the Lewis Acids and Bases that addition is selected is to combination, stirs.
If described Lewis Acids and Bases to or combination in solid block, melt can be directly added into or to press auxiliary square
Formula adds melt；
If described Lewis Acids and Bases to or combination in solid filament wire, can be with on-line automatic wire feeding mode, when casting even
Continuous addition, or it is cut into suitable segment, before casting every time, add casting ladle or scoop wooden dipper；
If described Lewis Acids and Bases to or combination in solid powdery, can select directly to blow to melt or with protection
Property the fluidized regime that drives of gas blow continuously, described in blow can select to insert melt from melt upper vertical blow,
Blow from body of heater side oblique cutting melt or blow from furnace bottom air brick hole.
Described Lewis Acids and Bases pair, active metal element selects to add melt, high-melting-point insoluble metal unit with protection form
Element selects coordination compound form, and readily soluble heavy metal selects elemental stage.
Described Lewis Acids and Bases to or combination, compound or coordination compound select to make pressed powder form in advance.
Described Lewis Acids and Bases to or combination, select to add melt after alloy host element melting completes, or molten
Add melt during body refine, or after refine purifies, add melt, or before cast form, add melt.
4, then above-mentioned alloy melt carrying out furnace refining, described refine selects to operate in enclosed environment, described envelope
Close environmental selection and get rid of, in convulsion mode, the waste gas that refine produces continuously.
5, remove the gred after refine, stand, sample analysis alloy composition, adjust chemical composition to regulation according to analysis result
Deviation range in；
Described adjustment selection of chemical composition by add Lewis Acids and Bases to or combination in the way of be adjusted；
Homoiothermic is to more than 650 DEG C, and aluminium alloy is come out of the stove, online degasification, slagging-off；
Described degasification can select the agitation of graphite-pipe sleeve rotor to be blown into purification gas；
Described purification gas can select nitrogen, argon, chlorine or their mixture；
Described slagging-off can select surface remove scum silica frost or select Filtration to remove in melt bottom thick particle or melt
Sediment；
Described Filtration can select ceramic filter plate or glass fibre or filter cloth as filter medium；
Described filtration can carry out single-stage filtration or double-stage filtering or multistage filtering；
Described thick particle can be the particle that granularity is not less than 10 microns.
6, casting.Selection centrifugal casting is poured into a mould, and step is as follows:
(1) melt proceeds to casting ladle from holding furnace；
(2) casting mold is preheating to preference temperature；
(3) open driving motor, band movable belt pulley and wheel shaft to rotate, and then drive the casting mold being mounted on an axle to rotate；
(4) adjustment casting mold rotating speed is 50～1500r/min, and the casting ladle that verts makes melt flow into running gate system along pouring basin, passes through
Running gate system flows into casting mold, is full of casting mold die cavity under casting mold rotary centrifugal force effect；
(5), after melt solidifies completely, stop the rotation, die sinking pickup.
(6) product, natural cooling, cleaning core, sawing rising head, polishing overlap are taken out in die sinking；
(7) appearance quality detection: rough casting, before carrying out presentation quality inspection, should be cleaned out smooth, non-machined surface
Dead head should be cleaned to cast(ing) surface and flush；
(8) internal soundness detection；
(9) 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 after being incubated at once, uses water-cooled or oil cold；
(10) ageing strengthening: the foundry goods completing solution treatment is sent into aging furnace and carries out ageing strengthening process, time below 230 DEG C
Effect strengthening, after insulation, natural cooling of coming out of the stove；
(11) sample analysis test checking；
(12) Practical Performance checking.
Part II: specific embodiment
Embodiment 1: the aluminium alloy of a kind of QT500 of replacement is throwed a spear dish and centre spinning method thereof
1, product parameter: diameter 1250mm, dish thickness 80mm；For there being woven fabric machine；
2, production procedure: melt → cast → rotation die cavity → mold filling and solidification → stall die sinking pickup → solid solution → timeliness；
3, alloy formula percentage by weight is:
Manganese Mn:0.6～0.7%, cadmium Cd:0.08%, copper Cu:6.3～6.5%；Ti ＜ 0.05%, Y ＜ 0.04%, Nd ＜ 0.13%, Mg
＜ 0.4%, Co ＜ 0.02%, ZrC ＜ 0.06%, surplus is aluminum Al；
4, melt cast temperature >=720 DEG C；
5, mold preheating temperature >=430 DEG C；
6, filling time≤10s；
7, die cavity rotating speed >=500r/min, retention time >=5 min；
8, heat treatment: T6 (solid solution adds complete artificial aging)；
9, cast microstructure index: metallographic structure is equiax crystal, mean grain size 90-95 μm, (T+ θ H) combination phase in crystal grain
Quantity 6/[μm]2；
10, foundry goods mechanical performance
| Tensile strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 520 | 450 | 142 | 6.2 |
Embodiment 2: the aluminium alloy of a kind of QT500 of replacement is throwed a spear dish and centre spinning method thereof
1, product parameter: diameter 1250mm, dish thickness 80mm；For there being woven fabric machine；
2, production procedure: melt → cast → rotation die cavity → mold filling and solidification → stall die sinking pickup → solid solution → timeliness；
3, alloy formula percentage by weight is:
Manganese Mn:0.6～0.7%, cadmium Cd:0.08%, copper Cu:6.3～6.5%；Ti ＜ 0.05%, Y ＜ 0.04%, Nd ＜ 0.13%, Mg
＜ 0.4%, Co ＜ 0.01%, ZrC ＜ 0.06%, surplus is aluminum Al；
4, melt cast temperature >=720 DEG C；
5, mold preheating temperature >=430 DEG C；
6, filling time≤10s；
7, die cavity rotating speed >=500r/min, retention time >=5 min；
8, heat treatment: T6 (solid solution adds complete artificial aging)；
9, cast microstructure index: metallographic structure is equiax crystal, mean grain size 90-95 μm, (T+ θ H) combination phase in crystal grain
Quantity 5/[μm]2；
10, foundry goods mechanical performance
| Tensile strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 510 | 440 | 135 | 6.2 |
Embodiment 3: the aluminium alloy of a kind of QT500 of replacement is throwed a spear dish and centre spinning method thereof
1, product parameter: diameter 1250mm, dish thickness 80mm；For there being woven fabric machine；
2, production procedure: melt → cast → rotation die cavity → mold filling and solidification → stall die sinking pickup → solid solution → timeliness；
3, alloy formula percentage by weight is:
Manganese Mn:0.6～0.7%, cadmium Cd:0.08%, copper Cu:5.3～6.5%；Co ＜ 0.02%, ZrC ＜ 0.06%, surplus is aluminum Al；
4, melt cast temperature >=720 DEG C；
5, mold preheating temperature >=430 DEG C；
6, filling time≤10s；
7, die cavity rotating speed >=500r/min, retention time >=5 min；
8, heat treatment: T6 (solid solution adds complete artificial aging)；
9, cast microstructure index: metallographic structure is equiax crystal, mean grain size 90-95 μm, (T+ θ H) combination phase in crystal grain
Quantity 5/[μm]2；
10, foundry goods mechanical performance
| Tensile strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 510 | 445 | 139 | 6.2 |
Claims (8)
1. one kind substitutes QT500 and throws a spear the aluminum alloy materials of dish, it is characterised in that: main constituent content by weight percentage: cobalt
Co:0.005%-0.02%；Manganese Mn :≤2%, cadmium Cd:0.05%～0.5%, copper Cu:4.2%～8.0% and Cu >=0.8Mn+4.05%；
Lewis Acids and Bases is to total amount 1% × 10-2～2.0%, making alloy mean grain size ＜ 120 microns, surplus is aluminum Al.
A kind of QT500 of replacement the most according to claim 1 throws a spear the aluminum alloy materials of dish, it is characterised in that: alloy grain
For equiax crystal.
A kind of QT500 of replacement the most according to claim 1 throws a spear the aluminum alloy materials of dish, it is characterised in that: alloy grain
Interior sub-nanometer (T+ θ H) combination phase amount reaches >=5/square micron.
A kind of QT500 of replacement the most according to claim 1 throws a spear the aluminum alloy materials of dish, it is characterised in that: described Louis
This acid-base pair is the one in the carbide of metal, main group dvielement, interior transition dvielement, or more than one mixing.
A kind of QT500 of replacement the most according to claim 4 throws a spear the aluminum alloy materials of dish, it is characterised in that: described gold
The carbide belonged to, including zirconium carbide ZrC.
6. throw a spear according to a kind of QT500 of replacement one of claim 1-5 Suo Shu the aluminum alloy materials of dish, it is characterised in that: institute
Stating Lewis Acids and Bases pair, account for Al matrix percentage by weight by element addition, scope is: Ti ＜ 0.05%, Y ＜ 0.04%, Nd ＜
0.13%, Mg ＜ 0.4%, ZrC ＜ 0.06%.
A kind of QT500 of replacement the most as claimed in claim 6 throws a spear the preparation method of aluminum alloy materials of dish, 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, as required
The alloy total amount of preparation, extrapolates 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) manganese Mn, cadmium Cd, copper Cu, cobalt Co are added, stirring, add selected Lewis Acids and Bases pair, or add selected Louis
This acid-base pair combines, and 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 to regulation according to analysis result
In deviation range；Homoiothermic is to more than 650 DEG C, and aluminium alloy is come out of the stove, online degasification, slagging-off；
(6) casting: use centrifugal casting cast.
A kind of QT500 of replacement the most according to claim 7 throws a spear the preparation method of aluminum alloy materials of dish, and its feature exists
In: described centrifugal casting is poured into a mould, and step is as follows:
(1) melt proceeds to casting ladle from holding furnace；
(2) casting mold is preheating to preference temperature；
(3) open driving motor, band movable belt pulley and wheel shaft to rotate, and then drive the casting mold being mounted on an axle to rotate；
(4) adjustment casting mold rotating speed is 50～1500r/min, and the casting ladle that verts makes melt flow into running gate system along pouring basin, passes through
Running gate system flows into casting mold, is full of casting mold die cavity under casting mold rotary centrifugal force effect；
(5), after melt solidifies completely, stop the rotation, die sinking pickup；
(6) product, natural cooling, cleaning core, sawing rising head, polishing overlap are taken out in die sinking；
(7) appearance quality detection: rough casting, before carrying out presentation quality inspection, should be cleaned out smooth, non-machined surface
Dead head should be cleaned to cast(ing) surface and flush；
(8) internal soundness detection；
(9) 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 after being incubated at once, uses water-cooled or oil cold；
(10) ageing strengthening: the foundry goods completing solution treatment is sent into aging furnace and carries out ageing strengthening process, time below 230 DEG C
Effect strengthening, after insulation, natural cooling of coming out of the stove；
(11) sample analysis test checking；
(12) Practical Performance checking.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610489541.4A CN105970040B (en) | 2016-06-29 | 2016-06-29 | A kind of replacement QT500 throws a spear the aluminum alloy materials and its centre spinning method of disk |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610489541.4A CN105970040B (en) | 2016-06-29 | 2016-06-29 | A kind of replacement QT500 throws a spear the aluminum alloy materials and its centre spinning method of disk |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105970040A true CN105970040A (en) | 2016-09-28 |
| CN105970040B CN105970040B (en) | 2018-06-29 |
Family
ID=57020115
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610489541.4A Expired - Fee Related CN105970040B (en) | 2016-06-29 | 2016-06-29 | A kind of replacement QT500 throws a spear the aluminum alloy materials and its centre spinning method of disk |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105970040B (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20120152414A1 (en) * | 2009-08-27 | 2012-06-21 | Yun Che | Multi-element heat-resistant aluminum alloy material with high strength and preparation method thereof |
| CN102517475A (en) * | 2011-12-15 | 2012-06-27 | 贵州华科铝材料工程技术研究有限公司 | ZrC-doped high strength aluminum alloy and preparation method thereof |
| CN103060645A (en) * | 2011-10-23 | 2013-04-24 | 贵州华科铝材料工程技术研究有限公司 | High-performance aluminum alloy material for manganese carbonyl complex deterioration and preparation method of material |
-
2016
- 2016-06-29 CN CN201610489541.4A patent/CN105970040B/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20120152414A1 (en) * | 2009-08-27 | 2012-06-21 | Yun Che | Multi-element heat-resistant aluminum alloy material with high strength and preparation method thereof |
| CN103060645A (en) * | 2011-10-23 | 2013-04-24 | 贵州华科铝材料工程技术研究有限公司 | High-performance aluminum alloy material for manganese carbonyl complex deterioration and preparation method of material |
| CN102517475A (en) * | 2011-12-15 | 2012-06-27 | 贵州华科铝材料工程技术研究有限公司 | ZrC-doped high strength aluminum alloy and preparation method thereof |
Non-Patent Citations (2)
| Title |
|---|
| 张中可等: "热处理对211Z.1铝合金组织及相结构的影响", 《特种铸造及有色合金》 * |
| 张彦华: "《工程材料与成型技术》", 28 February 2015 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105970040B (en) | 2018-06-29 |
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 | |
| CN106119620B (en) | A kind of replacement QT500 aluminium alloy differential mechanism materials and its gravitational casting forming method | |
| CN105970047A (en) | Aluminum alloy material for replacing QT500 agricultural machinery speed reducer and investment casting method thereof | |
| CN105937000B (en) | A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns | |
| CN105937003B (en) | A kind of aluminum alloy materials and its centrifugal casting forming method substituting QT500 major diameters transmission wheel disc | |
| CN105936999B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT450 Huff pipes | |
| CN105970041B (en) | A kind of aluminum alloy materials and its centre spinning method of replacement QT500 looms pump connecting seat | |
| CN106119639B (en) | A kind of aluminum alloy materials and its extrusion process for substituting QT500 transmission shafts | |
| CN105937001B (en) | A kind of aluminum alloy materials and its method for forging and molding for substituting QT600 blade of wind-driven generator | |
| CN105970039B (en) | A kind of aluminum alloy materials and its centre spinning method for substituting QT500 loom wheel hubs | |
| CN105936995A (en) | Aluminum alloy material replacing QT400 automobile control arm and semi-solid state die-casting forming method of aluminum alloy material | |
| CN105970056B (en) | A kind of replacement QT400 alloy electric machines brake cover and its centrifugal casting forming method | |
| CN106167869A (en) | A kind of aluminum alloy materials substituting QT500 loom jet part and metal mold gravity casting method thereof | |
| CN105970040A (en) | Aluminum alloy material substituting for QT500 picking disc and centrifugal casting method of aluminum alloy material | |
| CN105970042A (en) | Aluminum alloy material for replacing QT450 loom balance block and metal gravity casting method thereof | |
| CN106119635A (en) | A kind of replacement QT400 aluminium alloy flywheel caliper material and gravitational casting forming method thereof | |
| CN105950925B (en) | A kind of aluminum alloy materials and its extrusion process of replacement QT450 drive lead screws | |
| CN106119634A (en) | A kind of aluminum alloy materials substituting QT500 filter and gravity casting method thereof | |
| CN105970055B (en) | A kind of aluminum alloy materials and its centre spinning method substituting QT450 air caps | |
| CN106119636B (en) | A kind of aluminum alloy materials and its extrusion process for substituting QT500 blade wheels | |
| CN105950924B (en) | A kind of aluminum alloy materials and its swaging deformation method of replacement QT600 integrated valve blocks | |
| CN105936997A (en) | Aluminum alloy material replacing QT500 automobile axle housing and low-pressure casting forming method of aluminum alloy material | |
| CN105936998A (en) | Aluminum alloy material replacing QT450 automobile turbocharger shell and sand casting forming method of aluminum alloy material | |
| CN105937004B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT500 high pressure method orchids | |
| CN105970054A (en) | Aluminum alloy material for replacing QT450 vacuum single-chip hoop and sand model casting method thereof |
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 | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20180629 Termination date: 20210629 |