CN102534310A - High-strength aluminum alloy doped with Mo2C and MgH2 and preparation method thereof - Google Patents
High-strength aluminum alloy doped with Mo2C and MgH2 and preparation method thereof Download PDFInfo
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- CN102534310A CN102534310A CN201110421227XA CN201110421227A CN102534310A CN 102534310 A CN102534310 A CN 102534310A CN 201110421227X A CN201110421227X A CN 201110421227XA CN 201110421227 A CN201110421227 A CN 201110421227A CN 102534310 A CN102534310 A CN 102534310A
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Abstract
The invention discloses a high-strength aluminum alloy doped with Mo2C and MgH2 and a preparation method of the high-strength aluminum alloy. The preparation method comprises heating an Al ingot or melting Al to melt Al completely; adding Si, Fe, Cu, Mn, Mg, Zn and Ti, and completely dissolving and melting Si, Fe, Cu, Mn, Mg, Zn and Ti; refining and keeping the temperature at 700 DEG C to 1000 DEG C to obtain an alloy melt; feeding N2 or inert gas or the mixture containing arbitrary proportion of N2 and inert gas to degas and purify the alloy melt, and continuously feeding gas until the reaction finishes; adding the Mo2C and MgH2 powders to the alloy melt together with the above gas in a fluidized manner; stirring to realize uniform distribution of Mo2C and MgH2 in the alloy melt as well as full reaction with the alloy melt; standing, regulating temperature to 680 DEG C to 730 DEG C; and discharging molten alloy from the furnace, and casting. The high-strength aluminum alloy doped with Mo2C and MgH2 overcomes the disadvantage of poor performance of the prior aluminum alloy, and has improved strength and toughness, formability and hardenability, thereby providing high-end substrate for high-efficiency deep processing.
Description
Technical field
The present invention relates to a kind of aldural, also relate to its preparation method.
Background technology
The duraluminum that deep processing is used often need at first be cast as large-scale ingot blank; Like slab ingot, pole etc.; Through means such as rolling, extruding, forgings, be processed into various finished products again, these processes all will combine with heat treatment phase basically; 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 duraluminum 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-scale efficient deep processing, and be prefabricated into large-scale ingot blank, also be the technology critical point, first road whether test aluminum alloy materials itself is fit to carry out deep processing.
Aluminum alloy melt is in process of setting, and when volumetric shrinkage can not get feeding, the solidify position last at foundry goods just formed tubulose or branch hole such as forked, is called shrinkage cavity.It is shaped as irregular closed pores or open hole wall is coarse in the hole on surface, has dendritic structure.Because the final stage of eutectic board solidification and crystallization, so shrinkage cavity is easy to generate at the eutectic zone how and the position (thermal center place) of foundry goods final set.With Al-Si is the eutectic and the hypereutectic type duraluminum of base; Because the crystallization interval of alloy is little; The tendency of concentrate shrinking is big, concentrates shrinkage cavity so form tubulose easily in the short position of feeding a casting, sometimes because of the result of liquid filling shrinkage cavity that eutectic composition is arranged; Bigger eutectic segregation district or segregation layer can occur, especially around shrinkage cavity, form eutectic segregation easily.With Al-Cu, Al-Mg is the solid solution build duraluminum of base, and the crystallization interval broad forms the forked shrinkage cavity of branch easily at the insufficient position of feeding a casting.
Summary of the invention
In order to overcome the deficiency of prior art, the present invention provides a kind of aldural, selects the suitable alloy composition, avoids the formation of shrinkage cavity, for efficient deep processing provides high-end base material.
The technical solution adopted for the present invention to solve the technical problems is: a kind of aldural by percentage to the quality, comprises 0.4～0.8% Si; Fe smaller or equal to 0.7%, 0.15～0.4% Cu, Mn smaller or equal to 0.15%; 0.04～0.35% Cr, the Zn smaller or equal to 0.25%, Ti smaller or equal to 0.15%; 1.6～2.4% Mo, 0.1～0.15% C, 0.2～0.3% Mg, surplus is Al and unavoidable impurities; The content of every kind of impurity is no more than 0.05% of total mass per-cent, and the content of all impurity is no more than 0.15% of total mass per-cent.
The present invention also provides the preparation method of said aldural, adds Mo with the Combined Processing mode
2C and MgH
2, may further comprise the steps:
Step 1: the component according to said aldural is got the raw materials ready; Comprise the Si that accounts for total product mass percent 0.4～0.8%, the Fe smaller or equal to 0.7%, 0.15～0.4% Cu; Mn smaller or equal to 0.15%; 0.04～0.35% Cr, the Zn smaller or equal to 0.25%, Ti smaller or equal to 0.15%;
Step 2: in smelting furnace, add aluminium ingot or molten aluminum liquid earlier, heating makes it to melt fully, adds getting the raw materials ready of step 1 earlier by formula rate, makes it to dissolve fully and melt, and 700～1000 ℃ of insulations down, obtains alloy melt after the refining; Melting process is accomplished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion that alloy melt is carried out the degassing and purifying operation, and lasting ventilation finishes until reaction; To account for the Mo of total product mass percent 1.7～2.55% simultaneously
2C and 0.21～0.31% MgH
2Powder joins in the alloy melt with above-mentioned gas with the fluidization mode; Stir, make Mo
2C and MgH
2In alloy melt, be evenly distributed, and fully react with alloy melt; Leave standstill, temperature adjustment to 680～730 ℃, alloy liquid is come out of the stove, and carries out the Foundry Production of different goods respectively along following two kinds of flow processs.
Flow process one: the longshore current groove is toppled over and is come out of the stove, and to vertical water cooling casting machine system, casting processing use ingot blank, particularly above large-scale slab ingot of cast thickness 500mm and the pole more than the diameter 500mm.
Flow process two: metaideophone is gone 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 technology, the aluminum alloy casting of y alloy y foundry goods, particularly casting large-scale, thin-walled or complex construction.
The invention has the beneficial effects as follows:
The present invention provides a kind of aldural, selects the suitable alloy composition, avoids the formation of shrinkage cavity, for efficient deep processing provides high-end base material.
The invention solves high temperature insoluble metal element dissolving and the phase balance problem in aluminium alloy melt.Mo
2C and MgH
2Adding in the aluminium alloy melt process with protective gas with the fluidization form, have the specific surface area more much bigger than general cake mass, can realize disperseing fast and fully contacting with melt, significantly shortened and disperseed and the uniform time.
The present invention has caused multiple grain refining element, particle in molten aluminium, thickization that prevents matrix and strengthening phase had good result.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 mixtinite; Have high activity, a part of electronegativity of can reducing is higher than its carbide and nitride, even dissolving and dissociation reaction take place carbonitride; Decomposite atomic state C element and N element, also discharge dispersive atomic state refractory metal element own 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, further generate multiple intermetallic compound with aluminium again, and aluminium carbide and aluminium nitride AlN.
These metallic compounds when melt cools off 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 descends along with temperature and significantly reduces; So along with the cooling of melt, oversaturated melt is constantly separated out the intermetallic compound that is rich in alloying element, these compounds are in the intergranular enrichment; Be difficult for to each other merging, in microtexture, become thick intergranular compound group, alloy is produced crisp sclerosis influence; Worsen the alloy casting forming property, reduce its homogeneity, toughness, solidity to corrosion and through hardening performance.So; When alloy graining becomes the substruction of supersaturated solid solution matrix+intergranular metallic compound; Be commonly referred to pure as-cast structure, the alloy with this tissue just can have the mechanical property and other technical indicator of satisfying the demand after must passing through the thermal treatment of " solid solution+timeliness ".
Fe and Si form two kinds of Al-Fe-Si mutually easily in alloy, promptly α mutually with β mutually.α mutually in the lower and β of Si content mutually in Si content higher, and the former has tangible character outline, the latter then is minute hand shape and disc shaped.Since the existence of Mg in the alloy, the preferential and Mg generation Mg of Si
2The Si phase, remaining Si forms Chinese character shape α (Al mutually with Fe
12Fe
3Si), be a kind of thick tissue, be deleterious in alloy, 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.
The C of atomic state and N at high temperature are active, can form aluminide Al respectively with Al
4C
3And AlN, as previously mentioned, the fluidization of finely powdered adds, and makes carbonitride decompose the every kind of element that produces and all in melt, is the disperse distribution.
The AlN that N and Al reaction generates is an atomic crystal, belongs to the quasi-diamond nitride, the highlyest is stabilized to 2200 ℃; Room temperature strength is high, and intensity is slower with the rising decline of temperature, can effectively improve the hot strength and the resistance to corrosion of 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; The temperature when suitably regulating the cleaning molten operation and the concentration of protectiveness nitrogen, the content of AlN in the adjustable melt, 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 exists
Between, the shortest C-C key does
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, reaction as follows.
Joining the degree that the carbonitride in the melt decomposes, change along with the different of the stability of carbide, nitride itself and melt temperature, promptly react and have certain reversibility, is a kind of dynamic balance.The saturation solubility of most of transition element in molten aluminium is less, and this character of molten aluminium can find us and adds the wherein optimum proportion of carbonitride.After surpassing its saturation solubility; Part carbonitride just is present in the melt with molecular state; Because the molecular volume of simple solid matter structure carbide, nitride is all minimum, after solidifying, becomes gap phase disperse fully and is mounted in the matrix lattice, plays gap phase strengthening effect.
Because the stability order of the carbonitride that element forms is V＞Ti＞Nb＞W＞Mo＞Cr＞Mn＞Fe, this has determined the appearance order of the leading phase of metallic compound in the melt in proper order.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 metallic compound phases, improve intensity and ductility mutually then be formed with to be beneficial to.
Because the means of using the fluidization carbonitride to handle in the present invention; Integrate the multiple effects of strengthening matrix and crystal grain thinning; Replace master alloy, make duraluminum manufacturing concern no longer be limited by the master alloy manufacturer, help creating the green production line of " nearly moulding, short flow process, intensification "; Energy-saving and cost-reducing, reduce comprehensive cost; Simultaneously, in heat treatment process, owing to 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 sheet material that thickness 500mm is above and diameter 500mm are above) with " casting+heat treatment mode ", (realize " rolling " on the plate manufacturing technology of thickness 15～200mm) to cast generation at series specification.
The present invention has caused stable high interstitial atom and gap mutually in cooled aluminum substrate, becomes new efficient strengthening phase, and the intensity of material and hardness are improved.
The present invention adds 1.7～2.55% Mo in wrought aluminium alloy
2C and 0.21～0.31% MgH
2Powder can effectively increase heterogeneous forming core core in alloy graining process, thereby reaches the effect of grain refining, strengthens alloy strength; And the element that adds can promote to form interstitial atom and gap mutually; During high temperature in α (Al) sosoloid solubleness big, and very little when room temperature, thereby make alloy have higher heat-treatability matter; After the thermal treatment, its intensity and hardness all have significant improvement.
Below in conjunction with embodiment the present invention is further specified.
Embodiment
Embodiment 1:
A kind of aldural by percentage to the quality, comprises 0.4% Si, 0.7% Fe; 0.15% Cu, 0.15% Mn, 0.04% Cr, 0.25% Zn; 0.15% Ti, 1.6% Mo, 0.1% C, 0.2% Mg; Surplus is Al and unavoidable impurities, and the content of every kind of impurity is no more than 0.05% of total mass per-cent, and the content of all impurity is no more than 0.15% of total mass per-cent.
The present invention also provides the preparation method of said aldural, adds Mo with the Combined Processing mode
2C and MgH
2, may further comprise the steps:
Step 1: the component according to said aldural is got the raw materials ready, and comprises the Si that accounts for total product mass percent 0.4%, 0.7% Fe, 0.15% Cu, 0.15% Mn, 0.04% Cr, 0.25% Zn, 0.15% Ti;
Step 2: in smelting furnace, add aluminium ingot or molten aluminum liquid earlier, heating makes it to melt fully, adds getting the raw materials ready of step 1 earlier by formula rate, makes it to dissolve fully and melt, and 700～1000 ℃ of insulations down, obtains alloy melt after the refining; Melting process is accomplished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion that alloy melt is carried out the degassing and purifying operation, and lasting ventilation finishes until reaction; To account for the Mo of total product mass percent 1.7% simultaneously
2C and 0.21% MgH
2Powder joins in the alloy melt with above-mentioned gas with the fluidization mode; Stir, make Mo
2C and MgH
2In alloy melt, be evenly distributed, and fully react with alloy melt; Leave standstill, temperature adjustment to 680～730 ℃, alloy liquid is come out of the stove, and carries out the Foundry Production of different goods respectively along following two kinds of flow processs.
Flow process one: the longshore current groove is toppled over and is come out of the stove, and to vertical water cooling casting machine system, casting processing use ingot blank, particularly above large-scale slab ingot of cast thickness 500mm and the pole more than the diameter 500mm.
Flow process two: metaideophone is gone 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 technology, the aluminum alloy casting of y alloy y foundry goods, particularly casting large-scale, thin-walled or complex construction.
Embodiment 2:
A kind of aldural by percentage to the quality, comprises 0.6% Si, 0.5% Fe; 0.25% Cu, 0.1% Mn, 0.15% Cr, 0.2% Zn; 0.1% Ti, 2.0% Mo, 0.12% C, 0.25% Mg; Surplus is Al and unavoidable impurities, and the content of every kind of impurity is no more than 0.05% of total mass per-cent, and the content of all impurity is no more than 0.15% of total mass per-cent.
The present invention also provides the preparation method of said aldural, adds Mo with the Combined Processing mode
2C and MgH
2, may further comprise the steps:
Step 1: the component according to said aldural is got the raw materials ready, and comprises the Si that accounts for total product mass percent 0.6%, 0.5% Fe, 0.25% Cu, 0.1% Mn, 0.15% Cr, 0.2% Zn, 0.1% Ti;
Step 2: in smelting furnace, add aluminium ingot or molten aluminum liquid earlier, heating makes it to melt fully, adds getting the raw materials ready of step 1 earlier by formula rate, makes it to dissolve fully and melt, and 700～1000 ℃ of insulations down, obtains alloy melt after the refining; Melting process is accomplished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion that alloy melt is carried out the degassing and purifying operation, and lasting ventilation finishes until reaction; To account for the Mo of total product mass percent 2.12% simultaneously
2C and 0.26% MgH
2Powder joins in the alloy melt with above-mentioned gas with the fluidization mode; Stir, make Mo
2C and MgH
2In alloy melt, be evenly distributed, and fully react with alloy melt; Leave standstill, temperature adjustment to 680～730 ℃, alloy liquid is come out of the stove, and carries out the Foundry Production of different goods respectively along following two kinds of flow processs.
Flow process one: the longshore current groove is toppled over and is come out of the stove, and to vertical water cooling casting machine system, casting processing use ingot blank, particularly above large-scale slab ingot of cast thickness 500mm and the pole more than the diameter 500mm.
Flow process two: metaideophone is gone 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 technology, the aluminum alloy casting of y alloy y foundry goods, particularly casting large-scale, thin-walled or complex construction.
Embodiment 3:
A kind of aldural by percentage to the quality, comprises 0.8% Si, 0.5% Fe; 0.4% Cu, 0.09% Mn, 0.35% Cr, 0.1% Zn; 0.06% Ti, 2.4% Mo, 0.15% C, 0.3% Mg; Surplus is Al and unavoidable impurities, and the content of every kind of impurity is no more than 0.05% of total mass per-cent, and the content of all impurity is no more than 0.15% of total mass per-cent.
The present invention also provides the preparation method of said aldural, adds Mo with the Combined Processing mode
2C and MgH
2, may further comprise the steps:
Step 1: the component according to said aldural is got the raw materials ready, and comprises the Si that accounts for total product mass percent 0.8%, 0.5% Fe, 0.4% Cu, 0.09% Mn, 0.35% Cr, 0.1% Zn, 0.06% Ti;
Step 2: in smelting furnace, add aluminium ingot or molten aluminum liquid earlier, heating makes it to melt fully, adds getting the raw materials ready of step 1 earlier by formula rate, makes it to dissolve fully and melt, and 700～1000 ℃ of insulations down, obtains alloy melt after the refining; Melting process is accomplished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion that alloy melt is carried out the degassing and purifying operation, and lasting ventilation finishes until reaction; To account for the Mo of total product mass percent 2.55% simultaneously
2C and 0.31% MgH
2Powder joins in the alloy melt with above-mentioned gas with the fluidization mode; Stir, make Mo
2C and MgH
2In alloy melt, be evenly distributed, and fully react with alloy melt; Leave standstill, temperature adjustment to 680～730 ℃, alloy liquid is come out of the stove, and carries out the Foundry Production of different goods respectively along following two kinds of flow processs.
Flow process one: the longshore current groove is toppled over and is come out of the stove, and to vertical water cooling casting machine system, casting processing use ingot blank, particularly above large-scale slab ingot of cast thickness 500mm and the pole more than the diameter 500mm.
Flow process two: metaideophone is gone 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 technology, the aluminum alloy casting of y alloy y foundry goods, particularly casting large-scale, thin-walled or complex construction.
Claims (2)
1. doping Mo
2C and MgH
2Aldural, it is characterized in that: by percentage to the quality, comprise 0.4～0.8% Si; Fe smaller or equal to 0.7%, 0.15～0.4% Cu, Mn smaller or equal to 0.15%; 0.04～0.35% Cr, the Zn smaller or equal to 0.25%, Ti smaller or equal to 0.15%; 1.6～2.4% Mo, 0.1～0.15% C, 0.2～0.3% Mg, surplus is Al and unavoidable impurities; The content of every kind of impurity is no more than 0.05% of total mass per-cent, and the content of all impurity is no more than 0.15% of total mass per-cent.
2. said doping Mo of claim 1
2C and MgH
2The preparation method of aldural, it is characterized in that comprising the steps:
Step 1: the component according to said aldural is got the raw materials ready; Comprise the Si that accounts for total product mass percent 0.4～0.8%, the Fe smaller or equal to 0.7%, 0.15～0.4% Cu; Mn smaller or equal to 0.15%; 0.04～0.35% Cr, the Zn smaller or equal to 0.25%, Ti smaller or equal to 0.15%;
Step 2: in smelting furnace, add aluminium ingot or molten aluminum liquid earlier, heating makes it to melt fully, adds getting the raw materials ready of step 1 earlier by formula rate, makes it to dissolve fully and melt, and 700～1000 ℃ of insulations down, obtains alloy melt after the refining; Melting process is accomplished in enclosed environment;
Step 3: use the mixed gas of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion that alloy melt is carried out the degassing and purifying operation, and lasting ventilation finishes until reaction; To account for the Mo of total product mass percent 1.7～2.55% simultaneously
2C and 0.21～0.31% MgH
2Powder joins in the alloy melt with above-mentioned gas with the fluidization mode; Stir, make Mo
2C and MgH
2In alloy melt, be evenly distributed, and fully react with alloy melt; Leave standstill, temperature adjustment to 680～730 ℃, alloy liquid is come out of the stove.
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| CN 201110421227 CN102534310B (en) | 2011-12-15 | 2011-12-15 | High-strength aluminum alloy doped with Mo2C and MgH2 and preparation method thereof |
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| CN 201110421227 CN102534310B (en) | 2011-12-15 | 2011-12-15 | High-strength aluminum alloy doped with Mo2C and MgH2 and preparation method thereof |
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| CN102534310B CN102534310B (en) | 2013-06-26 |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104294070A (en) * | 2014-11-11 | 2015-01-21 | 安徽工业大学 | Method for preparing aluminum alloy containing magnesium through low temperature sintering |
| CN105200273A (en) * | 2015-10-15 | 2015-12-30 | 郭进标 | Platinum-doped aluminum alloy and preparation method thereof |
| CN106119620A (en) * | 2016-06-29 | 2016-11-16 | 贵州华科铝材料工程技术研究有限公司 | A kind of replacement QT500 aluminium alloy differential mechanism material and gravitational casting forming method thereof |
| CN112708805A (en) * | 2020-12-14 | 2021-04-27 | 华中科技大学 | Aluminum alloy mixed powder, method for improving density of aluminum alloy product and product |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE2134393A1 (en) * | 1970-07-13 | 1972-01-20 | Southwire Co | Aluminum alloy |
| CN102031421A (en) * | 2009-09-29 | 2011-04-27 | 贵州铝厂 | Cr-Gd high-strength heat-resistant aluminum alloy material and preparation method thereof |
-
2011
- 2011-12-15 CN CN 201110421227 patent/CN102534310B/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE2134393A1 (en) * | 1970-07-13 | 1972-01-20 | Southwire Co | Aluminum alloy |
| CN102031421A (en) * | 2009-09-29 | 2011-04-27 | 贵州铝厂 | Cr-Gd high-strength heat-resistant aluminum alloy material and preparation method thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104294070A (en) * | 2014-11-11 | 2015-01-21 | 安徽工业大学 | Method for preparing aluminum alloy containing magnesium through low temperature sintering |
| CN105200273A (en) * | 2015-10-15 | 2015-12-30 | 郭进标 | Platinum-doped aluminum alloy and preparation method thereof |
| CN106119620A (en) * | 2016-06-29 | 2016-11-16 | 贵州华科铝材料工程技术研究有限公司 | A kind of replacement QT500 aluminium alloy differential mechanism material and gravitational casting forming method thereof |
| CN112708805A (en) * | 2020-12-14 | 2021-04-27 | 华中科技大学 | Aluminum alloy mixed powder, method for improving density of aluminum alloy product and product |
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| CN102534310B (en) | 2013-06-26 |
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