CN102660693B - Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof - Google Patents
Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof Download PDFInfo
- Publication number
- CN102660693B CN102660693B CN 201110435467 CN201110435467A CN102660693B CN 102660693 B CN102660693 B CN 102660693B CN 201110435467 CN201110435467 CN 201110435467 CN 201110435467 A CN201110435467 A CN 201110435467A CN 102660693 B CN102660693 B CN 102660693B
- Authority
- CN
- China
- Prior art keywords
- aluminium alloy
- melt
- alloy
- alloy melt
- casting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Abstract
The invention relates to an aluminum alloy treated by using TiN powder and BeH2 powder, and a preparation method thereof. The process comprises the step of adding 1.0-2.0% of Ti element, 1.0-2.0% of N element and 1.0-2.0% of Be element in powder form into a melted deformation aluminum alloy, and the addition of the power in fluidized form into the aluminum alloy melt along with protective gases is such that a specific surface area which is much greater than common bulk materials is obtained, rapid dispersion and sufficient contact with the melt can be realized, and time for dispersion and time for uniform distribution are significantly shortened. At the same time, by using the high strength aluminum alloy of the invention in a casting process, heterogeneous nucleation cores can be increased effectively in an alloy solidification process, so that grain refining effect is achieved, and the strength of the cast alloy is enhanced. Moreover, the added elements can promote formation of interstitial atom and interstitial phase, solubility in alpha (Al) solid solutions is high at high temperature and is low at room temperature, so that the cast alloy has a high heat-processibility characteristic, and the strength and the hardness of the cast alloy are significantly improved after heat treatment.
Description
Technical field
The present invention relates to a kind of aldural, also relate to its preparation method.
Background technology
In the Al-Mg-Si-Cu line aluminium alloy due to composition and pouring technology improper, easily form high hardness compound.Especially for silicon content less than 12% (massfraction), the content of Mn+Fe is very easy to generate during higher than 0.8% (massfraction)
Al 12 Si (FeMn) 3 Compound.Because the hardness after this aluminium alloy shaping is higher, during mechanical workout, tool wear is serious, the white light tone hard point that as seen the surperficial naked eyes after processing are heaved, and microscopic examination hard point is bone shape or irregular particle shape.Composition through this hard point of power spectrum composition measurement consists of Al-Si-Mn-Fe, its form very easily with alloy in primary silicon obscure mutually.Part after the aluminium alloy with this hard point compound is shaped, poor in processability not only, and have a strong impact on the roughness of finished surface and the quality of anodic film.
Titanium becomes effective heterojunction nucleus because forming intermetallic compound in aluminium alloy, and the effect that suppresses the sosoloid crystal grain-growth is arranged and makes grain refining.But traditional addition means is to adopt the flux of Al-Ti master alloy or Al-Ti-B master alloy or Ti and B directly to add in aluminum alloy melt to go.
Because in alloying constituent or compound, density is large one-tenth branch is deposited in the foundry goods bottom, float on top on the little composition of density.For example add this refractory metal of Ti and Al for crystal grain thinning and form dystectic flaky compound Al
3Ti can early crystallize out from aluminium alloy, when growing up to the gravity segregation that just easily sinks to producing local rules when larger, can see the compound of the white bright ash of surfacing when segregation is more serious on the foundry goods fracture, primary silicon thick in hypereutectic Al-Si aluminium alloy also easily forms segregation because density is less.
In addition when this aluminium alloy before cast owing to stirring the inhomogeneous eutectic segregation that causes, concentrate the place in Eutectic Silicon in Al-Si Cast Alloys, the high fragility of hardness is large, the process tool wearing and tearing are large; The position that Eutectic Silicon in Al-Si Cast Alloys is few forms α (Al) sosoloid soft spots, and intensity is low, adds not only to glue cutter man-hour, worsens processing characteristics, can make the distortion of α (Al) sosoloid cause machined surface hickie to occur under the effect of cutting force.
Simultaneously, when adopting this aluminium alloy to cast, in the foundry goods that casting is completed, normal the appearance mainly contains oxide inclusion, molding material and flux mixture etc. various being mingled with.Wherein, be mingled with aluminum oxide the most general.Especially in containing the aluminium alloy of Mg, majority is mingled with and is aluminum oxide and magnesian mixture, so in the aluminium alloy smelting process, the content of oxide inclusion is one of important mark matter of reflection aluminium liquid metallurgical quality.
Be can prevent oxidation, the scaling loss, air-breathing of magnesium elements in the melting and casting of aluminium alloy, put forward the density of heavy alloyed metallurgical quality and surface film oxide, can also form compound with impurity F e, make needle-like iron become a shape, the recoil of foundry goods and model in the time of also can preventing from pouring into a mould.But the Al-Be master alloy is expensive, and this master alloy of melting is larger to the harm of human body.
This shows: 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
In order to overcome the deficiencies in the prior art, the invention provides a kind of employing TiN and BeH
2Aluminium alloy of powder treatment and preparation method thereof can overcome the deficiency that has aluminium alloy capability now, improves its obdurability, plasticity and hardening capacity, for efficient deep processing provides high-end base material.
A kind of employing TiN and BeH
2The aluminium alloy of powder treatment, it is characterized in that by percentage to the quality, comprise 0.4～0.8% Si, Fe less than or equal to 0.7%, 0.15～0.4% Cu, Mn less than or equal to 0.15%, 0.04～0.35% Cr, 0.8～1.2% Mg, the Zn less than or equal to 0.25%, 1.0～2.0% Ti, 0.29～0.58% N and 0.19～0.38% Be, surplus is Al and inevitable impurity, and the content of single contaminant is no more than 0.05% of total mass per-cent, and content of impurities is no more than 0.15% of total mass per-cent.
A kind of described employing TiN and BeH of preparing
2The method of the aluminium alloy of powder treatment is characterized in that step is as follows:
Step 1: aluminium ingot is added to heat in smelting furnace make it to melt fully, then add the Si of total product mass percent 0.4～0.8% by formula, Fe less than or equal to 0.7%, 0.15～0.4% Cu, Mn less than or equal to 0.15%, 0.04～0.35% Cr, 0.8～1.2% Mg, Zn less than or equal to 0.25% and less than or equal to 0.15% Ti dissolves fully and melts; Described melting process is completed in enclosed environment;
Step 2: insulation under 700～1000 ℃ obtains alloy melt;
Step 3: adopt mixed gas to carry out the degassing and purifying operation to aluminium alloy melt, and will account for the TiN of total product mass percent 1.29～2.58% and 0.23～0.46% BeH
2Powder joins in aluminium alloy melt with above-mentioned gas in the fluidization mode and mixes, and makes TiN and BeH
2Be evenly distributed in aluminium alloy melt, and continue ventilation until react complete; Described mixed gas is: nitrogen or rare gas element or nitrogen and rare gas element are mixed to get according to arbitrary proportion;
Step 4: temperature adjustment to 680 after reaction finishes～730 ℃ obtains the aluminium alloy melt that melting is completed.
Aluminium ingot in step 1 is replaced with molten aluminum liquid.
A kind of with described employing TiN and BeH
2The method that the aluminium alloy of powder treatment is cast, it is characterized in that: the aluminium alloy melt of claim 2 melting is toppled over along chute 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 diameter 500mm.
A kind of with described employing TiN and BeH
2The method that the aluminium alloy of powder treatment is cast, it is characterized in that: the aluminium alloy melt metaideophone of claim 2 melting is entered in the mold of foundry goods, use metal mold, sand mold or mixed type casting mode, adopt 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.
Employing TiN provided by the invention and BeH
2Aluminium alloy of powder treatment and preparation method thereof, in wrought aluminium alloy with Powdered 1.29～2.58% TiN and 0.23～0.46% the BeH of adding
2, add 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.Adopt simultaneously aldural of the present invention in castingprocesses, can effectively increase heterogeneous forming core core in alloy graining process, thereby reach the effect of grain refining, strengthen alloy strength; And the element that adds can promote to form interstitial atom and gap mutually, during high temperature in α (Al) sosoloid solubleness large, and very little when room temperature, thereby make alloy have higher heat-treatability matter, after thermal treatment, its intensity and hardness all have significant improvement.
Make a concrete analysis of as follows:
Without before adding above-mentioned element, except the common solution that form various elements, also contain Compound Phase that more following intermetallics form in melt at this alloy:
Mg
2Si phase, (FeMn)
3Si
2Al
15, α phase (Al
12Fe
3Si), S phase (Al
2CuMg);
these metallic compounds are when melt cooling, due to the minimum free energy principle of system, can not stable existence in the crystal grain that forms, to move and concentrate to crystal boundary under the driving that lattice distortion can differ from, simultaneously, saturation solubility due to alloying element in aluminum substrate descends along with temperature and significantly reduces, so cooling along with 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, become thick intergranular compound group in microtexture, alloy produces crisp hardening effect, worsen the alloy casting forming property, reduce 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 ".
Although, can improve through the thermal treatment of formulation optimization processing and raising alloy property, still still there are a lot of defectives in alloy itself: insufficient strength is high, can not cast large specification type ingot etc.
The present invention passes through alternative, the nitride of having developed transition element is processed the mode of melt, by adding appropriate Ti, N, Be element, produce Ti, the Be metal of atomic state after decomposing, do not had under the simple substance state between atoms metal with the d/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 solution and metallic compound altogether, and the leading phase when becoming crystallization and grain refining are mutually, are also the High-Temperature Strengthening phases simultaneously.Therefore, nitride adds in melt the decomposition that produces under high temperature and the disperse state of formation with fluidization, 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 nitrogen that is filled with in fusion process in addition is conducive to aluminium synthetic AlN in the nitrogen atmosphere of 800～1000 ℃.The AlN that generates due to N and Al reaction 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 decline is slower, can effectively carry heavy alloyed hot strength and resistance to corrosion; Thermal conductivity is good, and thermal expansivity is little, can improve the body material thermal shock resistance.Therefore, 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.So the concentration of the temperature when suitably regulating the cleaning molten operation and protectiveness nitrogen can be regulated the content of AlN in melt, this further provides method for the content of regulating transition metal in melt.
Joining in addition the degree that the nitride in melt decomposes, change along with the difference of the stability of nitride itself and melt temperature, namely 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 the maximum solid solution degree of dechromisation, titanium, vanadium, zirconium occurs in outside 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.
As seen: due to the means of using in the present invention the fluidization nitride 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 ", (realize " rolling to cast generation " on the plate of moderate thickness manufacturing technology of thickness 15～200mm) at series specification.
Generally speaking, the invention has the beneficial effects as follows:
Caused multiple grain refining element, particle in molten aluminium, thickization that prevents matrix and strengthening phase had good result.Caused stable high interstitial atom and gap mutually in cooled aluminum substrate, become new efficient strengthening phase, the intensity of material and hardness are improved.
The present invention is further described below in conjunction with embodiment.
Embodiment
Embodiment 1:
A kind of employing TiN and BeH
2The aluminium alloy of powder treatment by percentage to the quality, comprises 0.4% Si, 0.7% Fe, 0.15% Cu, 0.15% Mn, 0.04% Cr, 0.8% Mg, 0.25% Zn, 0.15% Ti, 1.0% Ti, 1.0% N, 1.0% Be, surplus is Al and inevitable impurity, 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 described aldural, adds TiN and BeH in the Combined Processing mode
2, comprise the following steps:
Step 1: the component according to described 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, 0.8% Mg, 0.25% Zn, 0.15% Ti;
Step 2: first add aluminium ingot or molten aluminum liquid in smelting furnace, heating makes it to melt fully, first adds getting the raw materials ready of step 1 by formula rate, makes it dissolve fully and melt, and after refining, insulation under 700～1000 ℃, obtain alloy melt; Melting process is completed in enclosed environment;
Step 3: use the mixed gas alloy melt of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion to carry out the degassing and purifying operation, and continue ventilation until react complete; To account for simultaneously the TiN of total product mass percent 1.0% and 1.0% BeH
2Powder joins in alloy melt with above-mentioned gas in the fluidization mode; Stir, make TiN and BeH
2Be evenly distributed in alloy melt, and fully react with alloy melt; Standing, temperature adjustment to 680～730 ℃ obtain the aluminium alloy melt that melting is completed.
Embodiment 2:
A kind of employing TiN and BeH
2The aluminium alloy of powder treatment by percentage to the quality, comprises 0.6% Si, 0.5% Fe, 0.25% Cu, 0.1% Mn, 0.15% Cr, 1.0% Mg, 0.2% Zn, 0.1% Ti, 1.5% Ti, 1.5% N, 1.5% Be, surplus is Al and inevitable impurity, 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 described aldural, adds TiN and BeH in the Combined Processing mode
2, comprise the following steps:
Step 1: the component according to described 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, 1.0% Mg, 0.2% Zn, 0.1% Ti;
Step 2: first add aluminium ingot or molten aluminum liquid in smelting furnace, heating makes it to melt fully, first adds getting the raw materials ready of step 1 by formula rate, makes it dissolve fully and melt, and after refining, insulation under 700～1000 ℃, obtain alloy melt; Melting process is completed in enclosed environment;
Step 3: use the mixed gas alloy melt of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion to carry out the degassing and purifying operation, and continue ventilation until react complete; To account for simultaneously the TiN of total product mass percent 1.5% and 1.5% BeH
2Powder joins in alloy melt with above-mentioned gas in the fluidization mode; Stir, make TiN and BeH
2Be evenly distributed in alloy melt, and fully react with alloy melt; Standing, temperature adjustment to 680～730 ℃ obtain the aluminium alloy melt that melting is completed.
Embodiment 3:
A kind of employing TiN and BeH
2The aluminium alloy of powder treatment by percentage to the quality, comprises 0.8% Si, 0.5% Fe, 0.4% Cu, 0.09% Mn, 0.35% Cr, 1.2% Mg, 0.1% Zn, 0.06% Ti, 2.0% Ti, 2.0% N, 2.0% Be, surplus is Al and inevitable impurity, 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 described aldural, adds TiN and BeH in the Combined Processing mode
2, comprise the following steps:
Step 1: the component according to described 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, 1.2% Mg, 0.1% Zn, 0.06% Ti;
Step 2: first add aluminium ingot or molten aluminum liquid in smelting furnace, heating makes it to melt fully, first adds getting the raw materials ready of step 1 by formula rate, makes it dissolve fully and melt, and after refining, insulation under 700～1000 ℃, obtain alloy melt; Melting process is completed in enclosed environment;
Step 3: use the mixed gas alloy melt of nitrogen or rare gas element or nitrogen and rare gas element arbitrary proportion to carry out the degassing and purifying operation, and continue ventilation until react complete; To account for simultaneously the TiN of total product mass percent 2.0% and 2.0% BeH
2Powder joins in alloy melt with above-mentioned gas in the fluidization mode; Stir, make TiN and BeH
2Be evenly distributed in alloy melt, and fully react with alloy melt; Standing, temperature adjustment to 680～730 ℃ obtain the aluminium alloy melt that melting is completed.
After the aldural liquid of employing the inventive method melting is come out of the stove, carry out respectively the Foundry Production of different goods along following two kinds of flow processs.
Flow process one: topple over along chute and 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 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.
Claims (5)
1. one kind is adopted TiN and BeH
2The aluminium alloy of powder treatment, it is characterized in that by percentage to the quality, comprise 0.4～0.8% Si, Fe less than or equal to 0.7%, 0.15～0.4% Cu, Mn less than or equal to 0.15%, 0.04～0.35% Cr, 0.8～1.2% Mg, the Zn less than or equal to 0.25%, 1.0～2.0% Ti, 0.29～0.58% N and 0.19～0.38% Be, surplus is Al and inevitable impurity, and the content of single contaminant is no more than 0.05% of total mass per-cent, and content of impurities is no more than 0.15% of total mass per-cent.
2. one kind prepares employing TiN claimed in claim 1 and BeH
2The method of the aluminium alloy of powder treatment is characterized in that step is as follows:
Step 1: aluminium ingot is added to heat in smelting furnace make it to melt fully, then add the Si of total product mass percent 0.4～0.8% by formula, Fe less than or equal to 0.7%, 0.15～0.4% Cu, Mn less than or equal to 0.15%, 0.04～0.35% Cr, 0.8～1.2% Mg, Zn less than or equal to 0.25% and less than or equal to 0.15% Ti melts fully and melts; Described melting process is completed in enclosed environment;
Step 2: insulation under 700～1000 ℃ obtains alloy melt;
Step 3: adopt nitrogen or rare gas element or nitrogen and rare gas element according to the mixed gas of arbitrary proportion, aluminium alloy melt to be carried out the degassing and purifying operation, and will account for the TiN of total product mass percent 1.29～2.58% and 0.23～0.46% BeH
2Powder joins in aluminium alloy melt with above-mentioned gas in the fluidization mode and mixes, and makes TiN and BeH
2Be evenly distributed in aluminium alloy melt, and continue ventilation until react complete;
Step 4: temperature adjustment to 680 after reaction finishes～730 ℃ obtains the aluminium alloy melt that melting is completed.
3. employing TiN according to claim 2 and BeH
2The method of the aluminium alloy of powder treatment is characterized in that:
Aluminium ingot in step 1 is replaced with molten aluminum liquid.
4. method that the aluminium alloy melt that melting claimed in claim 2 is completed is cast is characterized in that:
Aluminium alloy melt is toppled over along chute come out of the stove, to vertical water cooling casting machine system, casting processing ingot blank.
5. method that the aluminium alloy melt that melting claimed in claim 2 is completed is cast is characterized in that:
The aluminium alloy melt metaideophone is entered in the mold of foundry goods, use metal mold, sand mold or mixed type casting mode, adopt gravitational casting, pressure die casting or counter-pressure casting technique, Casting Aluminum Alloy Based.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201110435467 CN102660693B (en) | 2011-12-15 | 2011-12-22 | Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201110420851 | 2011-12-15 | ||
| CN201110420851.8 | 2011-12-15 | ||
| CN 201110435467 CN102660693B (en) | 2011-12-15 | 2011-12-22 | Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102660693A CN102660693A (en) | 2012-09-12 |
| CN102660693B true CN102660693B (en) | 2013-06-26 |
Family
ID=46770267
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 201110435467 Expired - Fee Related CN102660693B (en) | 2011-12-15 | 2011-12-22 | Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102660693B (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105369085A (en) * | 2015-12-15 | 2016-03-02 | 常熟市虹桥铸钢有限公司 | Casting alloy with good liquidity |
| CN106119636B (en) * | 2016-06-29 | 2018-06-29 | 贵州华科铝材料工程技术研究有限公司 | A kind of aluminum alloy materials and its extrusion process for substituting QT500 blade wheels |
| CN105937001B (en) * | 2016-06-29 | 2018-06-01 | 贵州华科铝材料工程技术研究有限公司 | A kind of aluminum alloy materials and its method for forging and molding for substituting QT600 blade of wind-driven generator |
| US20190291182A1 (en) * | 2018-03-23 | 2019-09-26 | GM Global Technology Operations LLC | Aluminum alloy powders for powder bed fusion additive manufacturing processes |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999031287A1 (en) * | 1997-12-12 | 1999-06-24 | Aluminum Company Of America | Aluminum alloy with a high toughness for use as plate in aerospace applications |
| CN1546709A (en) * | 2003-12-04 | 2004-11-17 | 尧 李 | Deformable aluminium alloy containing aluminum, zinc, magnesium, copper and beryllium |
| CN101285141A (en) * | 2008-05-30 | 2008-10-15 | 山西省运城安瑞节能风机有限公司 | Cast aluminum alloy material for mine-used parts |
| EP2177638A1 (en) * | 2008-10-15 | 2010-04-21 | "Impexmetal" S.A. | Aluminium alloy, in particular for heat exchangers manufacturing |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100741660B1 (en) * | 2006-02-28 | 2007-07-23 | 주식회사 대원합금 | Aluminum-magnesium alloy for interior & exterior furnishings of mobile phone and electronic products |
-
2011
- 2011-12-22 CN CN 201110435467 patent/CN102660693B/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999031287A1 (en) * | 1997-12-12 | 1999-06-24 | Aluminum Company Of America | Aluminum alloy with a high toughness for use as plate in aerospace applications |
| CN1546709A (en) * | 2003-12-04 | 2004-11-17 | 尧 李 | Deformable aluminium alloy containing aluminum, zinc, magnesium, copper and beryllium |
| CN101285141A (en) * | 2008-05-30 | 2008-10-15 | 山西省运城安瑞节能风机有限公司 | Cast aluminum alloy material for mine-used parts |
| EP2177638A1 (en) * | 2008-10-15 | 2010-04-21 | "Impexmetal" S.A. | Aluminium alloy, in particular for heat exchangers manufacturing |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102660693A (en) | 2012-09-12 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102424924B (en) | WN2 and LiBH4 powder added high-strength aluminum alloy and preparation method thereof | |
| CN102433475B (en) | High-strength and high-hardness aluminum alloy and preparation method thereof | |
| CN103060642A (en) | High-strength aluminum alloy subjected to carbonitride complex treatment and preparation method thereof | |
| CN102443725B (en) | High-strength aluminum alloy treated by AlH3 and preparation method of high-strength aluminum alloy | |
| CN102433472B (en) | High strength aluminium alloy and smelting and casting methods thereof | |
| CN102418007B (en) | High-temperature aluminum alloy treated by WB and LiH powder and preparation method of aluminum alloy | |
| CN102660693B (en) | Aluminum alloy treated by using TiN powder and BeH2 powder, and preparation method thereof | |
| CN103233138B (en) | Mg-Al series magnesium alloy grain-refining agent and preparation method thereof | |
| CN102534310B (en) | High-strength aluminum alloy doped with Mo2C and MgH2 and preparation method thereof | |
| CN102517475B (en) | ZrC-doped high strength aluminum alloy and preparation method thereof | |
| CN102418009B (en) | Aluminum alloy capable of digesting high-hardness compounds and smelting method of aluminum alloy | |
| CN110592442B (en) | Low-heat-conductivity high-toughness aluminum-manganese-cobalt die-casting aluminum alloy and preparation process thereof | |
| CN102418008B (en) | High-strength aluminum alloy obtained by removing inclusion through HfC and preparation method of aluminum alloy | |
| CN102433471A (en) | High-toughness aluminum alloy and preparation method thereof | |
| CN102505084B (en) | High-strength aluminum alloy added with TaC and preparation method for high-strength aluminum alloy | |
| CN102517476B (en) | High strength aluminum alloy capable of reducing porosity and dispersed shrinkage and preparation method thereof | |
| CN102433469B (en) | Smelting method of aluminium alloy co-dissolved with VC | |
| CN102433470B (en) | Aluminium alloy co-dissolved with TiAlN and CaH3 powder and smelting method | |
| CN102424925B (en) | Co2N-doped aluminium alloy and smelting method thereof | |
| CN102433473B (en) | WB-and-NaBH4-doped high-strength aluminum alloy and preparation method thereof | |
| CN102433474B (en) | NaH-doped high strength aluminium alloy and smelting method thereof | |
| CN102418011B (en) | High-strength aluminum alloy added with AlCrN and RbH and preparation method of aluminum alloy | |
| CN102560199B (en) | Use TiSiN and EuH2aluminium alloy of powder-processed and preparation method thereof | |
| CN102634702B (en) | A kind of doping Mg2c3high-strength aluminum alloy and preparation method thereof | |
| JP2004034135A (en) | Aluminum alloy with superior formability in semi-molten state and manufacturing method of its cast ingot |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| ASS | Succession or assignment of patent right |
Owner name: GUIZHOU ALUMINUM MATERIALS ENGINEERING TECHNOLOGY Free format text: FORMER OWNER: GUIZHOU HUAKE ALUMINIUM MATERIAL ENGINEERING TECHNOLOGY RESEARCH CO., LTD. Effective date: 20141103 |
|
| C41 | Transfer of patent application or patent right or utility model | ||
| COR | Change of bibliographic data |
Free format text: CORRECT: ADDRESS; FROM: 550014 GUIYANG, GUIZHOU PROVINCE TO: 550018 GUIYANG, GUIZHOU PROVINCE |
|
| TR01 | Transfer of patent right |
Effective date of registration: 20141103 Address after: 550018 B665 room, standard workshop auxiliary room, Jinyang science and Technology Industrial Park, Guiyang hi tech Zone, Guizhou Patentee after: Guizhou Aluminum Materials Engineering Technology Research Center Co., Ltd. Address before: 550014, Guizhou, Guiyang province Baiyun District aluminum alloy factory Road South Hospital Patentee before: Guizhou Huake Aluminium Material Engineering Technology Research Co., Ltd. |
|
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20130626 Termination date: 20131222 |