CN105937000B - A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns - Google Patents
A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns Download PDFInfo
- Publication number
- CN105937000B CN105937000B CN201610493118.1A CN201610493118A CN105937000B CN 105937000 B CN105937000 B CN 105937000B CN 201610493118 A CN201610493118 A CN 201610493118A CN 105937000 B CN105937000 B CN 105937000B
- Authority
- CN
- China
- Prior art keywords
- alloy
- casting
- ship
- aluminum alloy
- columns
- 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.)
- Expired - Fee Related
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
- 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 present invention discloses a kind of aluminum alloy materials substituting QT400 ship columns, it is characterised in that：Principal component content is by weight percentage：Lithium：0.4% 0.5%, 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；For Lewis Acids and Bases to total amount 1% × 10 4~2.0% or 7.0%~9.0%, it is aluminium Al to make 120 microns of alloy mean grain size ＜, surplus.
Description
Technical field
The present invention relates to a kind of aluminum alloy materials and preparation method thereof substituting QT400 ship columns.
Background technology
Stock number of the aluminium in the earth's crust is considerably beyond iron（Aluminium is 8.2wt%, iron 5.1wt%）, and the annual steel production in the whole world
1,200,000,000 tons of sales volume or more, aluminum metal volume of production and marketing only have 0.55 hundred million tons, this huge contrast fully reflect human society to aluminium and
The Resources and utilization level of aluminum material lags far behind the development of exploitation level to steel material.
Spheroidal graphite cast-iron（Abbreviation magnesium iron）It is one of the primary base material in steel industry, is heavily used for making extensively
Make stress complexity, the more demanding part such as intensity, toughness, wearability, such as universal machine, lifting, agricultural, automobile, casting, spinning
It knits, lathe, electric power, petrochemical industry, ship part etc., Main Morphology and type are hydraulic pressure shell, 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 widely used, but the manufacture of spheroidal graphite cast-iron production needs to carry out at very high temperatures, phase therewith
Corresponding energy consumption is also high, and pollution is big, and with the requirement that lightweight and energy conservation and environmental protection are constantly progressive, related spheroidal graphite cast-iron product is urgent
It needs to find new substitute.
In the technology upgrading of " with aluminium for steel ", in order to give full play to aluminium alloy with " light " the superior spy of series for representative
Property, it is necessary to so that it is had tremendous development in terms of " strong ", while there cannot be unacceptable manufacturing cost increment, it could significantly
It expands it and uses field.This requires must first make a breakthrough in Al-alloy material design.
It is examined closely from the method for material preparation, since material characteristics are combined by carry the microcosmic object of functionality of this feature
It contributes, therefore the good functional object of acquisition is combined, such as high intensity, high-melting-point, high-ductility, high rigidity, corrosion resistant
Erosion etc. is the final result that various preparation methods are pursued, to, the Design of Chemical Composition of aluminium alloy and its technology of preparing there is
Close internal integrity, this uniformity, in short, being the pass how a kind of atom is combined into required " object phase molecule "
System, the i.e. object of material mutually can regard a kind of molecular structure as.It is formulated the mixed smelting and casting crystalline of element, is fusion casting shape
The major contributing link of material of becoming a useful person phase molecule composite structure, in fusion-casting process, between solid solution crystal grain and the metal of crystal boundary
Compound molecule object mutually determines the crystalline state combination (submicron particles of alloy:10~300 μm or so of scale), subsequent heat treatment
Or flow harden is then to fine structure (micron particles under crystalline state group frame:1~30 μm or so of scale) or even more
Microcosmic precise and tiny structure (Subnano-class or sub-micron grade particle:1 μm of scale 10nm~＜) it is adjusted and perfect, this adjustment
With perfect degree and range, in known technology and traditional concept, it is believed that mainly by the alloy phase residing for alloy composition
The given combined decision of object of graph region, still, alloy phase diagram do not provide the addition of other trace elements and exclude generation
It influences, with less the directiveness for prediction addition and excluding other trace elements and mutually being influenced on object.Use for reference alloy solution chemistry
Theoretical and method improves melt structure, such as the covering of protective film, the addition of slag former, refining agent or alterant, degasification slagging-off
Purification etc., be improve alloy crystalline state combination, fine structure or even more microcosmic precise and tiny structure important technical, but these
Means, due to being to grope accumulation during prepare alloy to get, be often considered as " preparation process " rather than " at
Set up meter separately " part.
On engineer application, the size and state of aluminum alloy solution body crystal grain, and it is distributed in the intermetallic of crystal boundary
The size and form of object has conclusive influence to the mechanical property of alloy.Coarse plane crystalline substance, dendrite, column crystal etc. are no
Ordered crystal and the coarse brittle property intermetallic compound for being distributed in crystal boundary, can be the good fine structure of alloy and precise and tiny knot
Structure all balances out the obdurability contribution of matrix, because the law of development that these coarse grains are deferred to results from casting mold cavity
Type wall gives birth to core, from the unidirectionally extended growth pattern of export-oriented liquid internal, cause the component segregation of alloy, crystallization it is coarse it is unidirectional,
The non-uniform defect of macro property, to some common deficiencies as alloy, such as pin hole, stomata, shrinkage cavity and porosity, segregation, thick
The root of big solid solution, high hardness compound, crackle etc..The means of the routine rotten means and crystal grain thinning that use at present, such as
Add aluminium titanium boron or Al-Ti-C master alloy, best effect can only make mean grain size refine to 120~150 microns, and branch
The often not basic transformation of brilliant form, this is the important bottleneck problem that alloy mechanical property improves.Because being closed to aluminium
For gold, the approach that intensity and toughness improve simultaneously, the only refinement of crystal grain and rounding are obtained；The adjustment of heat treatment process,
In the state that crystalline structure has determined, intensity or toughness can only be made to be optimized on one side.Therefore, how further thin
Change the mean grain size with rounding alloy, is the target that industrial circle is pursued always.
In terms of material design angle, 211Z materials are difficult to overcome the problems, such as there is also some.Micro-analysis is found, is had
Bulky grain has very high titanium Ti and rare earth concentration, as promoting the substance of crystal grain refinement, this phenomenon to show Ti and rare earth
The opposite for needing to solve the problems, such as is moved towards；And in the production process of 211Z alloy-steel castings, also occur and common aluminum alloy
Equally common defect, including pin hole, stomata, shrinkage cavity and porosity, segregation, coarse 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 will start with from the chemical composition of alloy itself and its microcosmic phase structure of formation
It studies, especially the formation mechenism of object phase molecule composite structure is furtherd investigate, can just see clearly essence, and then finds solution
Certainly problem, the effective way of elimination defect.
It is saturating by the spherical aberration correction scanning for being up to the very high resolution of 0.08nm to aluminum bronze manganese systems (Al-Cu-Mn) alloy
The precise and tiny constituency analysis of electron microscope (STEM) is penetrated, various phase structures, the Atomic Resolution established on an atomic scale are obtained
It is distributed with chemical element.Confirm wherein there are a series of hardening constituents, including well-known Al-Cu binary metastable phase (areas GP,
θ ＂, θ ＇), new disc phase and balance phase θ (Al2Cu)；Wherein inside matrix grain, a kind of forked (the T+ θ H) group of stick of new discovery
Phase is closed, the trunk portion T-phase of the combination phase is Al-Cu-Mn ternary phases, molecular structural formula Al20Cu2Mn3, molecule phase character is
Diameter about 100nm, length about 600~1000nm are in mandrel shape and { 010 } face coherence in its (010) face and alloy matrix aluminum；And T
The apposition growth secondary phase of Al-Cu binary of size larger (thickness about 20nm, being about 50nm) around phase, due to the secondary phase with
Other Al-Cu metastable phases (areas GP, θ ＂, θ ＇ or other disc phases) are compared in matrix, have very big difference in structure, especially
Thickness is much thicker than other Al-Cu metastable phases, therefore the present invention is referred to as θ H phases, molecular structural formula Alx(x is likely less than Cu
2), it is a kind of richness Cu molecules.
According to alloy strengthening theory, the intensity of alloy is that material median surface or dislocation movement by slip are generated by the obstruction of particle
, obstruction is stronger, and the intensity of material is also bigger.And particle hinders the knot that behavior interacts with material median surface or dislocation movement by slip
Fruit, there are two types of：One is when particle strong hardness itself is not high enough, dislocation will cut through particle and continue to slide, and another kind is particle
Intensity is very high, and dislocation can not be cut through, then can only continue to slide around particle, and a circle dislocation ring is left around particle.
The size that two kinds of results contribute the strength of materials is obvious：Particle is cut through to the strength of materials around particle ratio
Contribution it is big；It cuts through particle and is capable of providing the preferable elongation percentage of material, and will be carried due to the humidification of dislocation ring around particle
For the higher yield strength of material and tensile strength.
Aluminium boat column has correlative study at home, but because of the limitation of basic material, mechanical property is relatively low, especially
It is tensile strength and poor corrosion resistance, has seriously affected the service life of ship column, increases the use cost using department and maintenance
Cost, or even increase security risk.
Invention content
The technical problem to be solved by the present invention is to：There is provided it is a kind of substitute QT400 ship columns aluminum alloy materials and its preparation side
Method, wherein addition Lewis Acids and Bases pair, effectively to expedite the emergence of critical nucleus（Obtain equiax crystal）, alloy is made to obtain before curing most
The good combined structure of molecule object（(T+ θ H) combines phase）, promote alloy crystalline state optimize, enable aluminum alloy to base material realize 400MPa and
Higher strength grade, to reach the Al-alloy products that production substitutes QT400 ship columns.
The technical scheme is that：A kind of aluminum alloy materials substituting QT400 ship columns, principal component content percentage by weight
Than meter：Lithium Li：0.4%-0.5%, 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%,
It is aluminium Al to make 120 microns of alloy mean grain size ＜, surplus.
The alloy grain is equiax crystal.
Sub-nanometer (T+ θ H) combination phase amount reaches >=1/square micron in the alloy grain.
The Lewis Acids and Bases are to for positive and negative ion body made of metal and ligand binding, complicated ligand compound, super large
Heteropoly compound, the nitride of metal, one kind in transition group dvielement or more than one mixing.
Cation body, anion body made of the metal and ligand binding include that chlordene closes chromium anion body
[CrCl6]3-。
The complicated ligand compound or super large heteropoly compound includes phosphotungstic acid H3[P(W3O10)4]。
The Lewis Acids and Bases pair account for Al matrix weight percent, ranging from by element additive amount：Zr ＜ 0.3%, W ＜
0.5%, Y ＜ 0.15%, [CrCl6]3-＜ 0.5%, WN2＜ 0.05%, H3[P(W3O10)4] ＜ 0.05%.
A kind of preparation method for the aluminum alloy materials substituting QT400 ship columns, comprises the steps of：
(1) weight ratio is determined within the scope of, element ratio, selecting one group of substance combination in aforementioned Lewis Acids and Bases, according to
The alloy total amount prepared is needed, the weight of each required material is extrapolated；
(2) aluminium ingot or molten aluminum liquid are added into smelting furnace, heat and is kept the temperature at 700 DEG C or more；
(3) manganese Mn, cadmium Cd, copper Cu is added, selected Lewis Acids and Bases pair are added in lithium Li stirrings, or are added selected
Lewis Acids and Bases stir evenly combination；
(4) and then to above-mentioned alloy melt furnace refining is carried out；
(5) slagging-off, standing, sampling analysis alloy composition after refining adjust chemical composition according to analysis result and extremely advise
In fixed deviation range；To 650 DEG C or more, aluminium alloy is come out of the stove for temperature adjustment, online degasification, slagging-off；
(6) it casts：It is poured into a mould using centrifugal casting.
The centrifugal casting cast, steps are as follows：
1. pourable casting after filtering；
2. should preheat mold before casting, sand core is installed, is blown clean mold cavity with compressed air；
3. starting centrifugal device, artificial cast or automation cast are taken, aluminium alloy is dipped out of stove with casting ladle and pours into mould
Have cast gate and cavity is full of by ingate；Natural cooling is strong cold；
4. product, natural cooling, cleaning sand core, sawing riser, polishing overlap are taken out in die sinking；
5. appearance quality detection：Rough casting should clean out smooth, non-processing face before carrying out presentation quality inspection
Dead head should be cleaned to cast(ing) surface and flush；
6. internal soundness detects；
7. solution treatment：The blank that casting is completed to roughing and inside and outside quality testing is sent into solid solution furnace, carry out 560 DEG C with
Lower solution treatment quenches after the completion of heat preservation, uses water cooling or oil cooling at once；
8. ageing strengthening：The casting for completing solution treatment is sent into aging furnace and carries out ageing strengthening processing, at 230 DEG C or less
Ageing strengthening, after heat preservation, natural cooling of coming out of the stove；
9. sampling analysis test verification；
10. practical performance is verified.
Beneficial effects of the present invention：It is pointed by lewis' theory of acids and bases, molecule solution can occur in aluminium alloy melt
Body or " acid-base pair " substance for contributing in time nano-area (range for being less than 1 nanometer) object phase molecule structure optimization, application
It is adjusted in the fine structure of melt nanoscale range, is the most important creative technological means of the present invention.
By using lewis' theory of acids and bases, make addition and exclusion to the trace element of carrying in relation to Lewis Acids and Bases,
Molecule disintegration and conversion occurs in aluminium alloy melt environment, to provide in the hyperfine microcell of melt (0.1nm~10nm scale models
Enclose) abundant disturbance and activation effect, reach and expedite the emergence of critical nucleus and largely formed, alloy grain degree is made further to be refined,
Form more rounding；Optimize very small areas (micron order simultaneously:1~30 μm or so of scale) and (Subnano-class is secondary in precise and tiny region
Micron order particle:1 μm of scale 10nm~＜) object phase molecule composite structure, increase (T+ θ H) combination mutually in alloy substrate
Content is the mechanism problem for the alloy strengthening that the present invention solves.
The aforementioned Lewis Acids and Bases of the present invention are to for positive and negative ion body made of metal and ligand binding, complicated ligand chemical combination
Object, super large heteropoly compound, the nitride of metal, one kind in transition group dvielement or more than one mixing.
For example, anion body [CrCl6]3-It is Louis's " acid-base pair ", the Cr that can receive electronics pair in substance+It is road
Lewis acid, the corresponding ligand-Cl for providing electronics pair is lewis base.
Cation body and anion body have ordinary matter can not be real alloy grain refinement as Louis " acid-base pair "
Existing excellent effect, this is because：These gas ions can be stabilized as normal material molecule at normal temperatures, and in aluminium
Molecule occurs in high temperature acid or alkali environment as alloy melt to disintegrate, generates lewis acid and lewis base；Due to being molecule solution
Body, so being a kind of " the falling apart " of the atom composite structure of secondary nanometer range, ligand moiety is come out with gaseous exhaust, is released
The core metal ion come is then reselected in conjunction with other atoms.
This disintegration and reconstruct being happened in aluminium alloy melt, it is different from common substance dissolving, because：1. under high temperature
Decomposing the incipient bubble that the gaseous material discharged is formed, only there are one molecular size (being less than 1nm, i.e. secondary nanophase), specific surface areas
Maximum has the disturbance ability of extremely strong activity and nanometer range, is in the size range that crystallization critical nucleus is formed, thus
The states such as fluctuation of energy, rise and fall of structure and composition fluctuations of atom rise and fall all with extremely strong in melt superfinishing microcell caused by and
Characteristics of Mutation promotes neighbouring more polyatom across crystallization potential barrier, so a large amount of formation of critical nucleus are particularly conducive to, to gold
The catalysis of compound reaction of formation and alloy structure crystal grain refinement all produce good better than common alterant such as aluminium titanium boron between category
Effect；Positive and negative ion body this disturbance and activation effect in the superfinishing microcell of secondary nanometer range simultaneously is conventional additional purification
What the bubble (diameter is more than 0.5mm) that gas is formed cannot achieve；2. the metallic atom or cation that decompose release have than matching
The specific surface area of body smaller volume and bigger, it is stronger to the disturbance and activation effect of neighboring atom, caused by superfinishing microcell
State fluctuating is more notable, also stronger to intermetallic compound reaction of formation catalysis and alloy substrate tissue Grain Refinement Effect；
It, will not be as common gold 3. division and reconstruct of the acid-base pair in high-temperature fusant enhance dispersion and diffusion velocity of the particle in microcell
Belong to or additive causes clustering like that, and restrained effectively caused by additive alloying component segregation and bulky grain matter
Point aggregation and grow up, this can effectively solve conventional grain fining agent coarsening tendency in crystallization process, such as can prevent
The roughening of titanium Ti and rare-earth phase；4. secondary reaction can also occur for ligand bubble, purification gas is accompanied after a series of variations
Discharge melt (for example generate CO2、CH4、N2、NH3Or H2S) or enter slag (such as Al2O3、Al(HO)3Or Al4C3), it is this net
Change acts on, can be with most stable of solid-state or gaseous material, and the H dissolved in the melt and oxide impurity absorbs and decomposition,
To which its catharsis is more preferable than conventional gas purification mode effect.Here it is positive and negative ion bodies as Lewis Acids and Bases pair
Addition and exclusion, aluminium alloy melt environment occur molecule disintegrate, atom reconstruct in acid-base chemical conversion and superfinishing microcell, to provide
Abundant disturbance in melt superfinishing microcell and activation effect reach and expedite the emergence of critical nucleus largely generation and the inhibition long your writing of crystal grain
With, and realize the mechanism of more preferable clean-up effect.By this mechanism, matrix crystalline state is made generally to become equiax crystal, grain size
Averagely it is less than 120 μm, it is average at 50~100 μm that further effect of optimization can reach grain size.This effect is to use merely
What the conventional grains such as aluminium titanium boron and aluminium titanium carbon fining agent and the gas purification technique of routine cannot achieve.
Complicated ligand compound, super large heteropoly compound also have alloy grain refinement general as Lewis Acids and Bases pair
The good result that logical substance cannot achieve can close because their molecular structure is similar with the structure of positive and negative ion body in aluminium
Atom reconstruct in disintegration, acid-base chemical conversion and the superfinishing microcell of molecule occurs in environment as golden melt, can also disintegrate in molecule
When release gaseous state or the ligand of liquid, purification gas discharge melt is accompanied after series reaction and (for example generates CO2、CH4、
N2、NH3Or H2S) or enter slag (such as NaCl, KCl, Al (HO)3、Al2O3Or Al4C3), wherein the metallic atom that discharges or from
Son, non-metallic atom or ion are all the ultra-fine fine particles of secondary nanophase, there is maximum specific surface area, and it is super to provide melt
Abundant disturbance in precise and tiny area and activation effect reach and expedite the emergence of critical nucleus and largely generate and crystal grain is inhibited to grow up the machine of effect
Reason.By this mechanism, matrix crystalline state is made generally to become equiax crystal, grain size is averagely less than 120 μm, further optimization
It is average at 50~100 μm that effect can reach grain size.This effect is thin using the conventional grains such as aluminium titanium boron and aluminium titanium carbon merely
What the gas purification technique of agent and routine cannot achieve.
When the external Lewis Acids and Bases being added in melt are to decomposing, the intermetallic compound with matrix Presence of an interface energy difference
Presoma is obviously also disturbed and activates and recurring structure rises and falls, and generates more critical nucleus, and (T+ θ H) combination is made mutually to exist
Concentration in alloy and be evenly distributed density, make up to 1/[μm]2More than, here it is Lewis Acids and Bases in nanoscale
Disturbance and activation effect can increase Subnano-class particle (T+ θ H) combination mutually and the areas nanoscale particle GP, θ ＂, θ ＇ series are strong
Change the mechanism of phase.
To sum up, Lewis Acids and Bases pair of the present invention can show as variform, including metal is formed with ligand binding
Positive and negative ion body, complicated ligand compound, super large heteropoly compound, the nitride of metal, one in transition group dvielement
Kind or more than one mixing.
In addition, since Lewis Acids and Bases are to being capable of providing to foreign peoples's material concentration of alloy melt bigger, increase
The constitutional supercooling degree of melt crystallization process causes nucleus quickly to cross critical dimension under stronger crystallization power, and in supercooling
It is freely nucleated and grows in liquid, being formed has isotropism and shape closer to spherical equi-axed crystal；Therefore avoid or
Component segregation, coarse unidirectional, the non-uniform defect of macro property of crystallization for alleviating alloy, to effectively avoid or alleviate conjunction
Some common deficiencies of gold, such as pin hole, stomata, shrinkage cavity and porosity, segregation, coarse solid solution, high hardness compound, crackle.
The present invention is based on to alloy microstructure very high resolution contrast image and precise and tiny constituency structural analysis, it was found that
It is transgranular that there is the hyperfine structures of the forked combination phase of (T+ θ H) stick of sub-micron grade.Compared with each binary of Al-Cu, (T+ θ H)
Combination mutually has many advantages, including：Particle size is big, and anti-dislocation movement by slip face is big；Trunk portion T is that high hard high stable compound is poly-
Rodlike twin made of conjunction can provide strength support around mode using dislocation as alloy；Its secondary θ H attachment is mutually on trunk
It is oblique or perpendicular to T mandrels direction and to surrounding matrix grow simultaneously with matrix coherence, enhance trunk to lattice-site around
The tightening ability of battle array, or, in other words, T mandrels by adhering to thereon to the secondary phases of θ H of surrounding growth, tightening act on to
The matrix space of surrounding is transmitted and diffusion, this effect, and steel in similar building structure is produced to matrix in secondary um region
Invigoration effect (can be described as " class concrete reinforced structure ") of the reinforced net in concrete, makes matrix strength greatly improve.This effect,
It is flake Al-Cu metastable phases in matrix (areas GP, θ ＂, θ ＇ or other disc phases) if compared from monomer
All far from compared to；But in common aluminum bronze manganese systems (Al-Cu-Mn) alloy, since each binary Al-Cu metastable phases exist
The distribution density of intrinsic silicon is significantly larger than the distribution density of (T+ θ H) combination phase, and the effect of (T+ θ H) combination phase is caused to be blanked
And it is never found.
(T+ θ H) combine phase in θ H but with different positions to much bigger thickness (about 20nm), alloy substrate is produced
Better than the reinforcing contribution with the binary Al-Cu metastable phases in the areas GP, θ ＂, θ ＇ or other disc shapeds existing for free state：θ H in addition to
The tightening of trunk T-phase is acted on peripherad matrix space transmission and diffusion is outer, due to anti-matrix slide surface bigger, therefore to matrix
Humidification bigger；Since direction is more, therefore isotropic uniformity is showed to the invigoration effect of matrix；Due to being not belonging to height
Rigid particle, so can still be supplied to the preferable plasticity and toughness of matrix in such a way that dislocation is cut through；In short, (T+ θ H) combination mutually optimizes
The object phase molecule composite structure of aluminum bronze manganese systems (Al-Cu-Mn) alloy provides being imitated around reinforcing for high Hard Inclusion T-phase for matrix
It should be acted on higher than metastable combined two kinds of the strengthening effects that cut through of free state Al-Cu；So research play it is this excellent comprehensive
Close effect, it is necessary to the emphasis of design of material concern from tradition merely it is metastable to Al-Cu it is combined be transferred out, and concentrate on pair
(T+ θ H) combination phase expedites the emergence of in effect.
Inventive formulation is configured as one of technical way, is to make the crystalline state of alloy combine to realize mean grain size ＜
Under the premise of 120 microns of equiax crystal, can also be achieved inside alloy grain (T+ θ H) combination phase amount 1/[μm]2More than.Cause
This, principal component content is by weight percentage：Lithium Li：0.4%-0.5%, 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%, it is aluminium Al to make 120 microns of alloy mean grain size ＜, surplus.By adding lithium Li in alloy
Middle formation Al2Li3、AlLi5Deng 5 kinds of dispersivity High-Temperature Strengthening phases, the hardness and corrosion resisting property of alloy can be improved, is mechanical index
Provide material base.
Specific implementation mode
The specific embodiment of the invention includes 2 parts, and first part is prompt and explanation, and second part is specific implementation
Example.
First part：Prompt and explanation
The centrifugal casting, steps are as follows：
1, using metal type dies, preheating is more than 350 DEG C；
2, aluminium ingot or molten aluminum liquid are added into smelting furnace for melting, heat and are kept the temperature at 700 DEG C or more；
3, alloying, is added manganese Mn, cadmium Cd, copper Cu, and selected Lewis Acids and Bases pair are added, or are added in lithium Li stirrings
Selected Lewis Acids and Bases stir evenly combination；
4 and then above-mentioned alloy melt refined with refining agent in stove；
5, slagging-off, standing, sampling analysis alloy composition after refining adjust chemical composition according to analysis result and extremely provide
Deviation range in；To 660 DEG C or more, aluminium alloy is come out of the stove for temperature adjustment, online degasification, slagging-off；
6, artificial cast or automation cast are taken after filtering, aluminium alloy is dipped out of stove with casting ladle, and to pour into mould gate logical
Ingate is crossed full of cavity and starts centrifugal casting；Natural cooling is strong cold；
7, product, natural cooling, cleaning surface molding sand, sawing riser, polishing overlap are taken out in die sinking；
8, appearance quality detection：Rough casting should clean out smooth, non-processing face before carrying out presentation quality inspection
Dead head should be cleaned to cast(ing) surface and flush；
9, internal soundness detects；
10, solution treatment：The blank that casting is completed to roughing and inside and outside quality testing is sent into solid solution furnace, carries out 560 DEG C
Following solution treatment quenches after the completion of heat preservation, uses water cooling or oil cooling at once；
11, ageing strengthening：Will complete solution treatment casting be sent into aging furnace carry out ageing strengthening processing, 230 DEG C with
Lower ageing strengthening, after heat preservation, natural cooling of coming out of the stove.
Second part：Specific embodiment
Embodiment 1
1, a kind of aluminum alloy materials composition by weight percent substituting QT400 ship columns is：Lithium Li：0.5%, copper Cu:5.4%,
Manganese Mn:0.6%, cadmium Cd:0.15%, zirconium Zr：0.2%, tungsten W：0.43%, yttrium Y：0.14%, chlordene closes chromium anion body [CrCl6]3-：
0.05%, tungsten nitride WN2：0.05%, phosphotungstic acid H3[P(W3O10)4]：0.05%；
2, preparation method：Melt → cast → rotation cavity → mold filling and solidification → stalling molds pickup → solid solution → timeliness；
3,660 DEG C of melt cast temperature ＞；
4,350 DEG C of mold preheating temperature ＞；
5, filling time ＜ 30s；
6,2 min of cavity rotating speed ＞ 500r/min, retention time ＞；
7, it is heat-treated：T6-solid solution adds full artificial aging；
8, cast microstructure index：Metallographic structure is equiax crystal, 80 ~ 100 μm of mean grain size, (T+ θ H) group in crystal grain
Close phase amount 2 ~ 4/[μm]2。
9, casting mechanical performance
| Power resistance strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 480 | 490 | 140 | 7.8 |
Embodiment 2
1, a kind of aluminum alloy materials composition by weight percent substituting QT400 ship columns is：Lithium Li：0.4%, copper Cu:5.5%,
Manganese Mn:0.8%, cadmium Cd:0.1%, zirconium Zr：0.2%, tungsten W：0.4%, yttrium Y：0.1%, chlordene closes chromium anion body [CrCl6]3-：
0.05%, tungsten nitride WN2：0.05%, phosphotungstic acid H3[P(W3O10)4]：0.05%；
2, specific preparation method is same as Example 1；
3, product microstructure index：Metallographic structure is equiax crystal, 80~120 μm of mean grain size, in crystal grain (T+ θ H)
Combine phase amount 2~3/[μm]2；
4, casting mechanical performance
| Power resistance strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 460 | 475 | 135 | 7.8 |
Embodiment 3
1, a kind of aluminum alloy materials composition by weight percent substituting QT400 ship columns is：Lithium Li：0.45%, copper Cu:2.5%,
Manganese Mn:0.8%, cadmium Cd:0.1%, phosphotungstic acid H3[P(W3O10)4]：0.05%；
2, specific preparation method is same as Example 1；
3, product microstructure index：Metallographic structure is equiax crystal, 80~120 μm of mean grain size, in crystal grain (T+ θ H)
Combine phase amount 2~3/[μm]2；
4, casting mechanical performance
| Power resistance strength Mpa | Yield strength Mpa | Hardness HB | Elongation after fracture % |
| 465 | 480 | 139 | 7.1 |
Claims (5)
1. a kind of aluminum alloy materials substituting QT400 ship columns, it is characterised in that：Principal component content is by weight percentage：Lithium Li：
0.4%-0.5%, 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；Surplus is aluminium Al；Additive total amount 1% × 10-4~2.0% or 7.0%~9.0%, so that alloy is averaged
120 microns of grain size ＜, sub-nanometer (T+ θ H) combination phase amount reaches >=1/square micron in alloy grain；In alloy grain
The molecular structural formula that sub-nanometer (T+ θ H) combines phase is (Al20Cu2Mn3+AlxCu)；Wherein x be less than 2, θ H phases thickness be 20nm,
A length of 50nm；The additive is phosphotungstic acid H3[P(W3O10)4], chlordene closes chromium anion body made of metal and ligand binding
[CrCl6]3-、WN2In one or more kinds of mixing or transition group dvielement in a kind of one kind with aforesaid compound
The above mixing.
2. a kind of aluminum alloy materials substituting QT400 ship columns according to claim 1, it is characterised in that：Alloy grain is
Equiax crystal.
3. a kind of aluminum alloy materials of replacement QT400 ship columns according to one of claim 1-2, it is characterised in that：It is described
Additive accounts for Al matrix weight percent, ranging from by element additive amount：Zr ＜ 0.3%, W ＜ 0.5%, Y ＜ 0.15%,
[CrCl6]3-＜ 0.5%, WN2＜ 0.05%, H3[P(W3O10)4] ＜ 0.05%.
4. a kind of preparation method of aluminum alloy materials substituting QT400 ship columns as claimed in claim 3, it is characterised in that：Packet
Containing following steps：
(1) within the scope of aforementioned additive, element ratio, one group of substance combination is selected, weight ratio is determined, prepares as needed
Alloy total amount extrapolates the weight of each required material；
(2) aluminium ingot or molten aluminum liquid are added into smelting furnace, heat and is kept the temperature at 700 DEG C or more；
(3) manganese Mn, cadmium Cd, copper Cu is added, selected additive is added in lithium Li stirrings, or selected additive combination is added,
It stirs evenly；
(4) and then to above-mentioned alloy melt furnace refining is carried out；
(5) slagging-off after refining is stood, sampling analysis alloy composition, and chemical composition is adjusted to defined according to analysis result
In deviation range；To 650 DEG C or more, aluminium alloy is come out of the stove for temperature adjustment, online degasification, slagging-off；
(6) it casts：It is poured into a mould using centrifugal casting.
5. a kind of preparation method of aluminum alloy materials substituting QT400 ship columns according to claim 4, it is characterised in that institute
Centrifugal casting cast is stated, steps are as follows：
1. pourable casting after filtering；
2. should preheat mold before casting, sand core is installed, is blown clean mold cavity with compressed air；
3. starting centrifugal device, artificial cast or automation cast are taken, out of stove aluminium alloy is dipped with casting ladle and pours into mold and pour
Mouth is full of cavity by ingate；Natural cooling is strong cold；
4. product, natural cooling, cleaning sand core, sawing riser, polishing overlap are taken out in die sinking；
5. appearance quality detection：Rough casting should be cleaned out smooth before carrying out presentation quality inspection, and non-processing face is poured
Riser should be cleaned to cast(ing) surface and flush；
6. internal soundness detects；
7. solution treatment：The blank that casting is completed to roughing and inside and outside quality testing is sent into solid solution furnace, carries out 560 DEG C or less admittedly
Molten processing quenches after the completion of heat preservation, uses water cooling or oil cooling at once；
8. ageing strengthening：The casting for completing solution treatment is sent into aging furnace and carries out ageing strengthening processing, in 230 DEG C or less timeliness
Strengthen, after heat preservation, natural cooling of coming out of the stove；
9. sampling analysis test verification；
10. practical performance is verified.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610493118.1A CN105937000B (en) | 2016-06-29 | 2016-06-29 | A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610493118.1A CN105937000B (en) | 2016-06-29 | 2016-06-29 | A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105937000A CN105937000A (en) | 2016-09-14 |
| CN105937000B true CN105937000B (en) | 2018-09-07 |
Family
ID=56872887
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610493118.1A Expired - Fee Related CN105937000B (en) | 2016-06-29 | 2016-06-29 | A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105937000B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109680170A (en) * | 2018-11-30 | 2019-04-26 | 江苏文灿压铸有限公司 | A kind of casting technique of the water-cooling motor cabinet for new-energy automobile |
| CN114058912B (en) * | 2022-01-17 | 2022-04-08 | 北京理工大学 | High-specific-strength and specific-stiffness aluminum-lithium alloy thick-wall annular piece and preparation method thereof |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2915391A (en) * | 1958-01-13 | 1959-12-01 | Aluminum Co Of America | Aluminum base alloy |
| CN102424924B (en) * | 2011-12-15 | 2013-05-15 | 贵州华科铝材料工程技术研究有限公司 | WN2 and LiBH4 powder added high-strength aluminum alloy and preparation method thereof |
| CN103160715B (en) * | 2011-12-19 | 2016-08-03 | 中国兵器科学研究院宁波分院 | A kind of Gradient Aluminium Alloy cylinder jacket material and preparation method thereof |
| CN103556018A (en) * | 2013-10-17 | 2014-02-05 | 常熟市良益金属材料有限公司 | High-strength alloy |
-
2016
- 2016-06-29 CN CN201610493118.1A patent/CN105937000B/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| CN105937000A (en) | 2016-09-14 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106119621B (en) | A kind of replacement aluminum alloy materials of QT450 braking automobile pump cases and its model casting forming method | |
| CN105937000B (en) | A kind of aluminum alloy materials and its centre spinning method substituting QT400 ship columns | |
| CN105970010B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT400 light-duty vehicle steering gears | |
| CN105936999B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT450 Huff pipes | |
| CN106119620B (en) | A kind of replacement QT500 aluminium alloy differential mechanism materials and its gravitational casting forming method | |
| CN105970047B (en) | A kind of aluminum alloy materials and its investment casting method for substituting QT500 agricultural machinery speed reducing machines | |
| CN105937002B (en) | A kind of aluminum alloy materials and its injection molding method substituting QT600 rolls | |
| CN105937003B (en) | A kind of aluminum alloy materials and its centrifugal casting forming method substituting QT500 major diameters transmission wheel disc | |
| CN105936995B (en) | A kind of aluminum alloy materials and its semisolid pressure casting forming method substituting QT400 automobile control arm | |
| CN106119634B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT500 filters | |
| CN105936998B (en) | A kind of replacement aluminum alloy materials of QT450 automobile turbocharger housings and its sand casting forming method | |
| CN105936997B (en) | A kind of aluminum alloy materials and its pressure casting forming method for substituting QT500 automobile axle housings | |
| CN105970041B (en) | A kind of aluminum alloy materials and its centre spinning method of replacement QT500 looms pump connecting seat | |
| CN105970055B (en) | A kind of aluminum alloy materials and its centre spinning method substituting QT450 air caps | |
| CN105970054B (en) | A kind of aluminum alloy materials and its sand mould casting method substituting magnesium iron QT450 vacuum list pin card hoops | |
| CN106065446B (en) | A kind of aluminum alloy materials and its sand mould casting method substituting QT400 well lids | |
| CN105937004B (en) | A kind of aluminum alloy materials and its gravity casting method substituting QT500 high pressure method orchids | |
| CN105970039B (en) | A kind of aluminum alloy materials and its centre spinning method for substituting QT500 loom wheel hubs | |
| CN105970052B (en) | A kind of aluminum alloy materials and its sand mould casting method for substituting QT500 heavy type car steering gears | |
| CN105970042B (en) | A kind of aluminum alloy materials and its metal mold gravity casting method substituting QT450 loom balance weights | |
| CN106119635B (en) | A kind of replacement QT400 aluminium alloys flywheel caliper material and its gravitational casting forming method | |
| CN106167869B (en) | A kind of aluminum alloy materials and its metal mold gravity casting method substituting QT500 loom jet parts | |
| CN105970040B (en) | A kind of replacement QT500 throws a spear the aluminum alloy materials and its centre spinning method of disk | |
| CN105936991B (en) | A kind of aluminum alloy materials and squeeze cast form method substituting QT500 automobile connecting bars | |
| CN105970050B (en) | A kind of aluminium alloy crane arm material and its sand mould casting method for substituting QT500 |
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 |
Granted publication date: 20180907 Termination date: 20210629 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |