CN103060642A - High-strength aluminum alloy subjected to carbonitride complex treatment and preparation method thereof - Google Patents
High-strength aluminum alloy subjected to carbonitride complex treatment and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a high-strength aluminum alloy subjected to carbonitride complex treatment and a preparation method thereof. The alloy comprises the following components in percentage by weight: 2.0-3.2 percent of Cu, less than or equal to 0.2 percent of Mn, 0.2-0.5 percent of Mg, less than or equal to 0.01 percent of Cr, less than or equal to 0.01 percent of Ni, less than or equal to 0.1 percent of Zn, less than or equal to 0.15 percent of Ti, less than or equal to 0.5 percent of Si, less than or equal to 0.5 percent of Fe, and the balance of Al and inevitable trace impurities, wherein the carbonitride MX(C,N)Y is 0.05-2.5 percent of total mass of the furnace burden. The aluminum alloy has the characteristics of high strength and good casting performance.
Description
Technical field
The present invention relates to a kind of aluminum alloy materials and high materialization treatment process, particularly aldural of a kind of carbonitride Combined Processing and preparation method thereof.
Background technology
The aluminium alloy that deep processing is used often needs at first to be cast as large-scale ingot blank, such as slab ingot, pole etc., again by means such as rolling, extruding, forgings, be processed into various finished products, these processes basically all will with the heat treatment phase combination, if to the finished product that can directly use, then also will be through operations such as over-segmentation, surface working, Passivation Treatment.These processing means need aluminum alloy materials itself to possess good deep processing performance, comprise castability, press working deformation performance, heat treatment reinforcement performance, corrosion resistance, antifatigue destructive characteristics, surface working and coating property etc.Wherein, founding performance is the basis of aluminium alloy deep processing performance.Large-scale ingot blank, especially the above above pole of slab ingot, slab and diameter 500mm of thickness 500mm, can be the representative base material of Large Efficient deep processing, and be prefabricated into large-scale ingot blank, also be the first technology critical point whether test aluminum alloy materials itself is fit to carry out deep processing.
According to statistics, in the world in the 500 various deformation aluminum alloy materials, the aluminium alloy that is usually used in the large-scale ingot blank of founding is less than 20, the aluminium alloy that wherein is most commonly used to the large-scale ingot blank of founding and produces slab has 5083,5026,6082,2017,2024,2219,7075,7050 etc., in these materials, what belong to duralumin and ultralumin category is 2XXX system and 7XXX system, and its slab is multiplex in aerospace industry, but the poor performance of the large-scale ingot blank of its founding, slab ingot and pole shaping rate are very low; 5XXX system, 6XXX are associated golden founding better performances, but intensity is low; Other then belongs to soft aluminium category such as 1XXX system, 3XXX line aluminium alloy.
The forming property of present aluminum alloy materials during except the large-scale ingot blank of founding is relatively poor, large-scale ingot blank is not high in the hardening capacity of heat treatment process, tempering resistance is relatively poor and can not satisfy higher mechanical property requirements or some property (as heat-resisting, anti-corrosion) etc., is significant deficiency yet.These defectives make it form the technology breakpoint that is difficult to cross in the process of the strong materials of weight such as field of engineering technology instead of steel goods and structure.
Summary of the invention
The problems such as technical problem to be solved by this invention is, the hardening capacity that the plasticity problem that exists at fusion-casting process for the aluminum current alloy and heat treatment process exist is not high add carbonitride M in the Combined Processing mode
x(C, N)
y, make it in melt, to be partly dissolved, atomic state alloying element M and C, N element are provided, cause the alterant element of multiple atomic state, a part of carbonitride still exists with compound form simultaneously, as the gap strengthening phase; Under the support of the acting in conjunction of atomic state, gap phase and Quick uniform distribution means, reach the deficiency that overcomes aluminium alloy capability, improve its obdurability, plasticity and hardening capacity, for efficient deep processing provides high-end base material.
Technical scheme of the present invention is, the aldural of carbonitride Combined Processing, by weight percentage, this alloying constituent is Cu:2.0～3.2%, Mn :≤0.2%, Mg:0.2～0.5%, Cr :≤0.01%, Ni :≤0.01%, Zn :≤0.1%, Ti :≤0.15%, Si :≤0.5%, Fe :≤0.5%, carbonitride M
X(C, N)
YBe 0.05～2.5% of furnace charge total mass, all the other are Al and inevitable trace impurity.
The aldural of carbonitride Combined Processing of the present invention, above-mentioned carbonitride M
X(C, N)
YRefer to that chemical formula is M
xC
yTransition metal carbide and chemical formula be M
xN
yThe transition metal nitride, and their mixture.
The aldural of carbonitride Combined Processing of the present invention, carbonitride M
X(C, N)
YIn M refer to be positioned in the periodic table of elements metallic element that IIIB～VIII B family, First Transition are tied to the 3rd transition system, comprise rare earth element, iron group and platinum group.
The aldural of carbonitride Combined Processing of the present invention, above-mentioned carbonitride M
X(C, N)
YIn M refer to Hf, Zr, Ti, Ta, Nb, V, W, Mo, Cr, Mn, Co, Ni or RE.
The aldural of carbonitride Combined Processing of the present invention, above-mentioned carbonitride M
X(C, N)
YThe actual molecules structure type comprise: simple solid matter structural carbon compound (M
xC, x=1～2) or nitride (M
xN, x=1～2), complicated solid matter structural carbon compound is (with M
3C, M
7C
3, M
23C
6Be main), the duplex carbide (partly replace, such as Fe by atoms metal
3W
3C, Fe
21Mo
2C
6) and the carbonitride that dissolves each other (C and N atomic component are replaced, such as Ti (C, N), (Cr, Fe)
23(C, N)
6).
The aldural of carbonitride Combined Processing of the present invention, above-mentioned carbonitride M
x(C, N)
yThe aldural of Combined Processing, M
x(C, N)
yPhysical aspect be pulverulent solids, the state of aggregation granularity is the 20-200 order.
The preparation method of the aldural of carbonitride Combined Processing of the present invention comprises the steps:
Step 1: in above-mentioned element ratio scope, a selected group element and carbonitride, the alloy total amount of preparation is as required again extrapolated the quality of every kind of required elemental metals, establishment alloy production allocation sheet, and get the raw materials ready by allocation sheet choosing foot;
Step 2: add aluminium ingot or molten aluminum liquid first in smelting furnace, heating makes it to melt fully, adds first the selected alloying element of step 1 by formula rate, makes it to dissolve fully and melt insulation under 700～1000 ℃ after the refining; Melting process is finished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element, add a small amount of chlorine, melt is carried out the degassing and purifying operation, the carbonitride powder is joined in the alloy melt with gas in the fluidization mode; Stir simultaneously, carbonitride is evenly distributed in alloy melt, and fully react with alloy melt; Alterant adds complete, continues to pass into protective gas to reacting complete; Leave standstill, temperature adjustment to 680～730 ℃, aluminium alloy is come out of the stove, and carries out respectively the Foundry Production of different goods along following two kinds of flow processs.
Flow process one: topple over along chute and to come out of the stove, to vertical water cooling casting machine system, the large-scale slab ingot that casting processing ingot blank, particularly cast thickness 500mm are above and the pole more than the diameter 500mm.
Flow process two: metaideophone enters in the mold of foundry goods, uses metal mold, sand mold or mixed type casting mode, adopts gravitational casting, pressure die casting or counter-pressure casting technique, the aluminum alloy casting of Casting Aluminum Alloy Based, particularly casting large-scale, thin-walled or complex construction.
Compared with prior art, the present invention has following major advantage:
1, solved high temperature insoluble metal element dissolving and the phase balance problem in aluminium alloy melt.
2, in molten aluminium, caused multiple grain refining element, particle, thickization that prevents matrix and strengthening phase had good result.
3, in cooled aluminum substrate, caused stable high interstitial atom and gap mutually, become new efficient strengthening phase, the intensity of material and hardness are improved.
Particularly, the present invention has the following advantages.
The powder formed carbon nitride has the specific surface area more much bigger than general cake mass adding in the aluminium alloy melt process with protective gas with the fluidization form, can realize disperseing fast and fully contacting with melt, has significantly shortened and has disperseed and the uniform time.
Carbonitride is in the high temperature aluminum melt, because aluminium itself is exactly the fabulous metal of electroconductibility at normal temperatures, in the hot environment more than 700 ℃, its molten state is a kind of high-density unbound electron and aluminum ions mixture, have high activity, a part of electronegativity of can reducing is higher than its carbide and nitride, even dissolving and dissociation reaction occur carbonitride, decomposite atomic state C element and N element, also discharge the atomic state refractory metal element that itself disperses simultaneously; These elements that decompose out further with reactive aluminum, generate various reinforcement facies pattern materials and rotten formulation material; These atomic state materials react with aluminum substrate at once, at first dissolve in matrix and form common solution, after reaching capacity again further and aluminium generate compound between various metals, and aluminium carbide and aluminium nitride.Reaction process is as follows:
M
x(C, N)
y+ e (high temperature) → xM (atomic state)+yC (atomic state)+yN (atomic state)
M+Al (liquid) → α (Al) is solution → saturated altogether solution → cooling → supersaturated solid solution altogether
M+Al (saturated altogether solution) → M-Al (intermetallic compound)
C (atomic state)+Al (liquid) → Al
4C
3(compound)
N (atomic state)+Al (liquid) → AlN (compound)
When system is in steady state, M
x(C, N)
yWith α (Al) saturated altogether solution/supersaturated solid solution and intermetallic compound (M-Al)+Al
4C
3Reach the content balance in melt between compound+AlN compound.
At this alloy without adding M
x(C, N)
yBefore the carbonitride, except the common solution that forms various elements, also contain the Compound Phase that more following intermetallics form in the melt:
θ phase (CuAl
2), Mg
2Si phase, N phase (Al
7Cu
2Fe), α phase (Al
12Fe
3Si), S phase (Al
2CuMg).
These metallic compounds are when melt cooling, because the minimum free energy principle of system, can not stable existence in the crystal grain that forms, will be under the driving that lattice distortion can differ from move and concentrate to crystal boundary, simultaneously, because the saturation solubility of alloying element in aluminum substrate significantly reduces along with drop in temperature, so cooling along with melt, oversaturated melt is constantly separated out the intermetallic compound that is rich in alloying element, and these compounds are difficult for merging in the intergranular enrichment to each other, in microtexture, become thick intergranular compound group, alloy produces crisp hardening effect, worsens the alloy casting forming property, reduces its homogeneity, toughness, solidity to corrosion and through hardening performance.So, when alloy graining becomes the basic structure of supersaturated solid solution matrix+intergranular metallic compound, be commonly referred to pure as-cast structure, the alloy with this tissue must just can have mechanical property and other technical indicator of satisfying the demand after the thermal treatment through " solid solution+timeliness ".
Fe and Si easily form two kinds of Al-Fe-Si mutually in alloy, and namely α phase and β are mutually.α mutually in the lower and β of Si content mutually in Si content higher, and the former has obvious character outline, latter is minute hand shape and disc shaped.Because the existence of Mg in the alloy, Si preferential with Mg generation Mg
2The Si phase, remaining Si and Fe form Chinese character shape α phase (Al
12Fe
3Si), be a kind of thick tissue, in alloy, be harmful to, but institute's refinements such as a small amount of transition element that this thick tissue can be existed in the matrix such as Mn, Ni, Cu, Cr, V, Mo, W.Cu, Mn in the present invention's prescription have just played this thinning effect.
But even process and improve the thermal treatment of alloy property through this formulation optimization, still there are a lot of defectives in alloy: insufficient strength is high, can not cast large specification type ingot etc.
By adding the M of furnace charge total mass 0.05～2.5%
x(C, N)
y, solved these defectives.Its know-why is as follows.
The first, the M metal of atomic state comprises: rare earth element---Sc, Y, La, Ce, Pr, Nd, Po, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb or Lu; IVB family element---Ti, Zr, Hf; VB family element---V, Nb, Ta; Group vib element---Cr, Mo, W; VIIB family element---Mn, Tc, Re; Iron group in the VIII family---Fe, Co, Ni; Platinum group in the VIII family---Ru, Rh, Pd, Os, Ir, Pt.
The atomic radius great majority of these elements are different from aluminium, difference 5% with interior (greater than 135.6pm less than 150pm) except Ti, Nb, Mo, Tc, Pd, Ta, W, Re, Ir, Pt, all the other are all above 5%, can cause so the strong distortion of lattice, form larger distortional strain energy, when the saturation solubility of element in molten aluminium large, and the solid solubility under the room temperature hour, system is solidified the lattice distortion of generation can be also large, be equivalent to the part heat content of system under the condition of high temperature with lattice distortion can form be stored in the structure; When lattice distortion can evenly distribute in microtexture, the macro property of whole material was improved: such as intensity, ductility, stress corrosion resistant ability etc.Otherwise, when lattice distortion energy skewness, when particularly concentrating on crystal boundary, produce powerful potential energy of stress between the strengthening phase, Grain Boundary Character has represented the feature of whole material, and material just demonstrates hard fragility and susceptibility-to-corrosion, large tearing tendency is arranged when casting, coarse grains both easily ftractureed when solution hardening, reduced again hardening capacity.
Producing powerful lattice distortion and can and make it to be evenly distributed in microtexture, is the fundamentals of designing material excellent properties, particularly mechanical property.In the present invention, Cu and Mg be large with Al atomic radius difference, be again simultaneously two kinds of elements of liquid easily molten, solid-state indissoluble, Al sosoloid and a series of strengthening phase that they form, make material possess large lattice distortion energy, admittedly but can not guarantee at liquid → can reach the even distribution of distortional strain energy under the microtexture state when changing, so caused fault in material.
Utilizing the high-melting-point element at first to separate out in process of cooling becomes leading phase, is difficult for again simultaneously the characteristics of growing up, and makes it to lead on every side melt crystallization separate out, and can reach the even distribution under microtexture of grain refining, distortional strain energy.
But being in the high-melting-point element of simple substance state, is extremely insoluble in the aluminium molten system below 1000 ℃; With the general active nonmetal compound that generates such as reactions such as O, F, Cl, can be used as alterant and add molten aluminium, generating stabilizer pole Al with the Al reaction
2O
3, AlF
3, AlCl
3The time discharge atomic state refractory metal atom, but because O, F, electronegativity and very large ionic radius that the Cl element is very strong had both easily formed the difficult compound compound that decomposes of cluster-shaped in melt, do not have amalgamation with matrix, can worsen alloy property.
The present invention is by alternative, and the carbonitride of having developed transition element is processed the mode of melt.The atomic state M metal that carbonitride after the decomposition produces, do not had under the simple substance state between atoms metal with the d/f/s electronics potential barrier that the lattice energy of tightly packed generation between the powerful metal bond energy that produces and similar atom forms of combining closely, merge with " naked attitude " and a large amount of matrix atom on every side, form altogether solution and metallic compound, and the leading phase when becoming crystallization and grain refining are mutually, also are the High-Temperature Strengthening phases simultaneously.
Therefore, carbonitride M
x(C, N)
yFluidization adds the decomposition that produces in the melt under the high temperature and the disperse state of formation, solved refractory metal and dissolve difficult, the even difficult problem that distributes in aluminium liquid, realized lattice distortion can the distribution of microcosmic homogenizing and the refinement of crystal grain.
The second, the C of atomic state and N.The C of atomic state and N at high temperature are active, can form respectively aluminide Al with Al
4C
3And AlN, as previously mentioned, the fluidization of finely powdered adds, and all is the disperse distribution so that carbonitride decomposes the every kind of element that produces in melt.
The AlN that N and Al reaction generates is atomic crystal, belongs to the quasi-diamond nitride, the highlyest is stabilized to 2200 ℃; Room temperature strength is high, and the rising of intensity temperature descend slower, hot strength and resistance to corrosion that can the Effective Raise alloy; Thermal conductivity is good, and thermal expansivity is little, can improve the body material thermal shock resistance; Because AlN also can be synthetic in 800～1000 ℃ nitrogen atmosphere by aluminium; therefore; temperature when suitably regulating the cleaning molten operation and the concentration of protectiveness nitrogen can be regulated the content of AlN in the melt, and this further provides method for the content of regulating transition metal in the melt.
The Al that C and Al reaction generate
4C
3Be a kind of ionic crystal of complex construction, fusing point reaches 2100 ℃; Atoms metal can be 4,5,6 coordinations in practical structures, and Al-C bond distance is at 1.90-2.22
Between, the shortest C-C key is 3.16
X ray is studied then has single carbon atom with discrete carbanion C in the display structure
4-Form exists; The aluminium carbide particle can reduce the trend of material creep, improves body material hardness; Have strong suction H effect, can effectively remove the atom H of the existence in the melt, react as follows.
Al
4C
3+12[H]→4Al+3CH
4
By reaction as seen, an aluminium carbide molecule can be removed 12 H atoms, is a kind of efficient degasification material.
Simultaneously, Al
2O
3Building-up reactions also can occur in-C-N system under the melt environment, generate AlN and Al
4C
3
2Al
2O
3+6C→Al
4C
3+3CO
2↑
Al
2O
3+5N→2AlN+3NO↑
Therefore, to have slagging-off (mainly be Al in these two reactions
2O
3) effect.
The 3rd, join the degree that the carbonitride in the melt decomposes, change along with the different of the stability of carbide, nitride itself and melt temperature, namely react and have certain reversibility, be a kind of dynamic balance.The saturation solubility of most of transition element in molten aluminium is less, and the maximum solid solution degree of dechromisation, titanium, vanadium, zirconium occurs in outside the peritectic temperature, and the maximum solid solution degree of other elements all occurs in eutectic temperature; Solubleness at room temperature is all less than 0.1%wt.
This character of molten aluminium can find us and adds the wherein optimum proportion of carbonitride.After surpassing its saturation solubility, a part of carbonitride just is present in the melt with molecular state, because simple solid matter structural carbon compound (M
xC, x=1～2), nitride (M
xN, x=1～2) molecular volume is all minimum, becomes gap phase disperse fully and be mounted in the matrix lattice after solidifying, and plays gap phase strengthening effect.
And complicated solid matter structural carbon compound is (with M
3C, M
7C
3, M
23C
6Be main), the duplex carbide (partly replace, such as Fe by atoms metal
3W
3C, Fe
21Mo
2C
6) and the carbonitride that dissolves each other (C and N atomic component are replaced, such as Ti (C, N), (Cr, Fe)
23(C, N)
6), in melt and matrix, both can be decomposed into carbide, the nitride of simple solid matter structure, also can receive and molten and multiple transition element, after crystallization, become strengthening phase.
Because the stability order of the carbonitride that element forms is V＞Ti＞Nb＞W＞Mo＞Cr＞Mn＞Fe, this has sequentially determined the appearance order of the leading phase of metallic compound in the melt.Thick N phase (Al to impurity F e formation
7Cu
2Fe), α phase (Al
12Fe
3Si) all have the pinning crystal boundary and hinder the effect that its crystal boundary moves, thus refinement these complicated metal compound phases, improve intensity and ductility mutually then be formed with to be beneficial to.
The 4th, in the present invention, in order to increase the activity of indissoluble carbonitride and matrix reaction, add fashionablely in fluidization, suitably use Cl
2, with nitrogen N
2And rare gas element (He or Ar) together, and the powder formed carbon nitride is sent into melt; And in melt, have enough when active when carbonitride, just only adopt nitrogen N
2Mixture with rare gas element.
Work as N
2When being filled with the high temperature aluminium alloys melt, itself just had the activity of giving birth to reaction with the various metals golden hair, at this moment, need to according to this activity in melt of carbonitride, regulate N
2Ratio with rare gas element.
The 5th, because the means of using in the present invention the fluidization carbonitride to process, the multi-effect of strengthening matrix and crystal grain thinning is integrated, replace master alloy, make aluminium alloy manufacturing concern no longer be limited by the master alloy manufacturer, be conducive to create the Green line of " nearly moulding, short flow process, intensive ", energy-saving and cost-reducing, reduce comprehensive cost; Simultaneously, in heat treatment process, owing to having formed excellent material microstructure, the unrelieved stress of ingot blank is less, therefore can significantly improve thermal treatment usefulness, improve the hardening capacity of ingot blank, when comparing with similar alloy, can produce thicker blank (bar that the sheet material that thickness 500mm is above and diameter 500mm are above) with " casting+heat treatment mode ", (the plate of moderate thickness manufacturing technology of thickness 15～200mm) realizes " rolling to cast generation " at series specification.
Description of drawings:
Fig. 1 is the total reaction figure of carbonitride in the high temperature aluminum melt.
Embodiment
Step 1: the selected every element of according to the form below and material formula, and by the alloy total amount 1000kg for preparing, extrapolate the weight of every kind of required material.
Step 2: add aluminium ingot or molten aluminum liquid first in smelting furnace, heating makes it to melt fully, adds first the selected alloying element of step 1 by formula rate, makes it to dissolve fully and melt insulation under 700～1000 ℃ after the refining; Melting process is finished in enclosed environment;
Step 3: the mixed gas that uses nitrogen and argon gas (V/V 1: 1), add a small amount of chlorine (volume ratio: 1%), melt is carried out the degassing and purifying operation, carbonitride powder (50 order) is joined in the alloy melt with gas in the fluidization mode; Stir simultaneously, carbonitride is evenly distributed in alloy melt, and fully react with alloy melt; Alterant adds complete, continues to pass into mixed gas to reacting complete; Leave standstill, temperature adjustment to 680～730 ℃, aluminium alloy is come out of the stove, and carries out respectively the Foundry Production of different goods along following two kinds of flow processs.
Flow process one: topple over along chute and to come out of the stove, to vertical water cooling casting machine system, the large-scale slab ingot that casting processing ingot blank, particularly cast thickness 500mm are above and the pole more than the diameter 500mm.
Flow process two: metaideophone enters in the mold of foundry goods, uses metal mold, sand mold or mixed type casting mode, adopts gravitational casting, pressure die casting or counter-pressure casting technique, the aluminum alloy casting of Casting Aluminum Alloy Based, particularly casting large-scale, thin-walled or complex construction.
Annotate: the material that uses in step 1, the ratio of each material and actual the varying in weight of allocating into, all the other steps of each embodiment are all just the same.
Claims (6)
1. one kind
The aldural of carbonitride Combined Processing, it is characterized in that: by weight percentage, this alloying constituent is Cu:2.0～3.2%, Mn :≤0.2%, Mg:0.2～0.5%, and Cr :≤0.01%, Ni :≤0.01%, Zn :≤0.1%, Ti :≤0.15%, Si :≤0.5%, Fe :≤0.5%, carbonitride M
X(C, N)
YBe 0.05～2.5% of furnace charge total mass, all the other are Al and inevitable trace impurity.
2. according to claim 1
The aldural of carbonitride Combined Processing,It is characterized in that: above-mentioned carbonitride M
X(C, N)
YRefer to that chemical formula is M
xC
yTransition metal carbide and chemical formula be M
xN
yThe transition metal nitride, and their mixture.
3. according to claim 2
The aldural of carbonitride Combined Processing,It is characterized in that: carbonitride M
X(C, N)
YIn M refer to be positioned in the periodic table of elements metallic element that III B～VIII B family, First Transition are tied to the 3rd transition system, comprise rare earth element, iron group and platinum group.
4. according to claim 3
The aldural of carbonitride Combined Processing,It is characterized in that: above-mentioned carbonitride M
X(C, N)
Y InM refers to
Hf, Zr, Ti, Ta, Nb, V, W, Mo, Cr, Mn, Co, Ni or RE.
5. according to claim 1
The aldural of carbonitride Combined Processing,It is characterized in that: above-mentioned carbonitride M
x(C, N)
y The aldural of Combined Processing,M
x(C, N)
yPhysical aspect be pulverulent solids, the state of aggregation granularity is the 20-200 order.
6. described according to claim 1-5
The preparation method of the aldural of carbonitride Combined Processing,It is characterized in that: comprise the steps:
Step 1: in above-mentioned element ratio scope, a selected group element and carbonitride, the alloy total amount of preparation is as required again extrapolated the quality of every kind of required elemental metals, establishment alloy production allocation sheet, and get the raw materials ready by allocation sheet choosing foot;
Step 2: add aluminium ingot or molten aluminum liquid first in smelting furnace, heating makes it to melt fully, adds first the selected alloying element of step 1 by formula rate, makes it to dissolve fully and melt insulation under 700～1000 ℃ after the refining; Melting process is finished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element, add a small amount of chlorine, melt is carried out the degassing and purifying operation, the carbonitride powder is joined in the alloy melt with gas in the fluidization mode; Stir simultaneously, carbonitride is evenly distributed in alloy melt, and fully react with alloy melt; Alterant adds complete, continues to pass into protective gas to reacting complete; Leave standstill, temperature adjustment to 680～730 ℃, aluminium alloy is come out of the stove, and carries out respectively the Foundry Production of different goods along following two kinds of flow processs;
Flow process one: topple over along chute and to come out of the stove, to vertical water cooling casting machine system, the large-scale slab ingot that casting processing ingot blank, particularly cast thickness 500 ㎜ are above and the pole more than diameter 500 ㎜;
Flow process two: metaideophone enters in the mold of foundry goods, uses metal mold, sand mold or mixed type casting mode, adopts gravitational casting, pressure die casting or counter-pressure casting technique, the aluminum alloy casting of Casting Aluminum Alloy Based, particularly casting large-scale, thin-walled or complex construction.
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| CN108517431A (en) * | 2018-05-17 | 2018-09-11 | 天长市正牧铝业科技有限公司 | A kind of production technology of High-tenacity high-strength aluminium alloy bars bat materials |
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| CN112899516A (en) * | 2021-01-15 | 2021-06-04 | 广东省科学院材料与加工研究所 | Zirconium-containing aluminum-based alloy and preparation method and application thereof |
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| CN105177360A (en) * | 2015-06-29 | 2015-12-23 | 安徽越天特种车桥有限公司 | Friction increase type composite aluminum alloy automobile part mixed with sepiolite fibers and casting technology of friction increase type composite aluminum alloy automobile part |
| CN105886846A (en) * | 2016-05-18 | 2016-08-24 | 太仓鸿鑫精密压铸有限公司 | Corrosion-resistant aluminum alloy die casting |
| CN108246999A (en) * | 2018-03-14 | 2018-07-06 | 富钛金属科技(昆山)有限公司 | A kind of semi-solid-state metal compression molding process |
| CN108517431A (en) * | 2018-05-17 | 2018-09-11 | 天长市正牧铝业科技有限公司 | A kind of production technology of High-tenacity high-strength aluminium alloy bars bat materials |
| CN110527883A (en) * | 2019-09-18 | 2019-12-03 | 江苏集萃精凯高端装备技术有限公司 | A kind of high temperature resistant cast aluminium alloy gold and preparation method thereof containing Cu-Mn-Mg |
| CN110527873A (en) * | 2019-09-29 | 2019-12-03 | 合肥工业大学 | A kind of chassis auxiliary frame Al-Si-Mg-Ti-N-Sc alloy and preparation method thereof |
| CN111621719A (en) * | 2020-07-07 | 2020-09-04 | 西安工业大学 | High-strength heat-resistant die-casting aluminum alloy and smelting method |
| CN112899516A (en) * | 2021-01-15 | 2021-06-04 | 广东省科学院材料与加工研究所 | Zirconium-containing aluminum-based alloy and preparation method and application thereof |
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