CN1600466A - Method for preparing block of nano aluminum alloy in ultrahigh strength - Google Patents
Method for preparing block of nano aluminum alloy in ultrahigh strength Download PDFInfo
- Publication number
- CN1600466A CN1600466A CN200410009661.7A CN200410009661A CN1600466A CN 1600466 A CN1600466 A CN 1600466A CN 200410009661 A CN200410009661 A CN 200410009661A CN 1600466 A CN1600466 A CN 1600466A
- Authority
- CN
- China
- Prior art keywords
- temperature
- alloy
- ball milling
- weight
- hours
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Landscapes
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Abstract
A process or preparing high-strength nano-Al alloy block includes providing the Al-Zn-Mg-Cu-Zr-Ni alloy, prefabricating alloy ingot by induction furnace, aerosolizing to obtain alloy powder, low-temp ball grinding in liquefied nitrogen, and high-pressure treating at medium or low temp.
Description
Technical field
The invention belongs to aluminium alloy and nano material preparation technical field, a kind of preparation method of superhigh intensity block nanometer aluminium alloy particularly is provided.This material can be applicable to the key structure spare in fields such as Aeronautics and Astronautics, military project, electromechanics, automobile and micromachine.
Background technology
The research of block nanometer structural material and application are important directions of nano material development, further developing and using and have very important effect whole nanometer material science technology.Though laboratory research has proved the performance of nano structural material and has been far superior to traditional coarse grain material (Zhang Lide, Mu Jimei, nano material and nanostructured, Science Press, Beijing, 2001, p260), but the conversion process that the laboratory research achievement is used to engineering but obviously lags behind.One of them main obstacles is that the preparation forming technique of block nanometer material achieves no breakthrough, and promptly obtains be easier to relative with small sample of powder with nanostructured, and obtains to satisfy block materials difficulty many of practical structures application requirements.By the nano powder preparation block materials, generally need through a series of densified forming process, its key is to control growing up of crystal grain in densification process, therefore requires at first to prepare the nano-powder with high thermal stability.In recent years, the low temperature ball grinding technique has in preparation and has obtained important breakthrough (D.Witkin, Z.Lee, R.Rodrigurz, S.Nutt, E.J.Lavernia.Scripta Mater., 2003 aspect the nano-powder of high heat stability; 49:297; F.Zhou, X.Z.Liao, Y.T.Zhu, S.Dallek, E.J.Lavernia, Acta Materialia, 2003; 51:2777).The applicant is at patent of invention " a kind of liquid nitrogen cryogenics ball milling prepares the method for high thermal stability nano-powder " (application number: describe relevant ins and outs 200410000066.7) in detail.This technology and middle low temperature are forced worker's technology combine, can prepare high performance block nanometer structural material.
Aluminium alloy has low, the easy processing of proportion, low cost and other advantages as most typical light material in the metal material, is a kind of dual-use material of key always.With Al-Zn-Mg-Cu (7xxx) be alloy be the high-strength/tenacity aluminum alloy of representative be 20th century the '30s be to grow up gradually on the basis of alloy at Al-Zn-Mg, optimize and revise through constantly carrying out composition recent decades, simultaneously, make the ultimate tensile strength (σ of alloy in conjunction with the improvement of continuing to optimize to conventional cast and deformation processing, subsequent heat treatment technology
b) scope is increased to 630～680MPa from 500 early stage～580MPa, plasticity, fracture toughness and the decay resistance of material also are improved simultaneously.But along with the Zn content in the alloy increases, the hot cracking tendency in gross segregation in the material and the ingot casting process strengthens, and badly influences the final serviceability of the lumber recovery and the material of ingot casting.Adding does not have breakthrough aspect traditional preparation process, shaping and the Study on Processing Technology exploitation at aluminium alloy, causes the ultimate tensile strength (σ of this class alloy
b) the very difficult 700MPa high point of breaking through.Entered since the eighties,, make the Development of New Generation high-strength/tenacity aluminum alloy become a reality along with the practicability of non-equilibrium material preparation technology such as rapid solidification.
Aspect the exploitation of ultrahigh-intensity high-toughness aluminium alloy, be that the industrially developed country of representative all adopts advanced technology of preparing to succeed in developing to contain Zn to measure more than the 8 weight % (to be up to 14 weight %) in the early 1990s, σ with the U.S., Japan, Britain, Germany, France, Italy
bBe 780～810MPa, δ
10Be 8～13% ultra-high-strength aluminum alloy product of new generation, and be used to make parts in structural member, the structure member in the aerospace vehicle, bullet train key structure spare, automobile and other sports equipment in the fuel for nuclear power plant manufacture key equipment etc.The high-strength/tenacity aluminum alloy of China is to grow up from imitated basis, is subjected to the restriction of historical conditions and the influence of other various factors, and low-level and imitated material is many, and innovative material is few.The annual now required high-strength aluminum alloy of a large amount of foreign exchange imports that still need expend of China.Also have considerable high strength alumin ium alloy owing to politics cause, can not import.Along with China enters WTO and the fast development of using the high-strength/tenacity aluminum alloy industry, the demand of such material will sharply increase.
The fast development of nano material technology at present provides new opportunity for the development of China's high-performance aluminium alloy.The alloy that selection has the improved strength potentiality in existing aluminum alloy series, utilize mechanical alloying to drive the effect of " away from equilibrium state ", improve the alloy element content in original alloy and handle its performance is increased substantially, can reach the purpose of further raising aluminium alloy capability by nanometer.
Summary of the invention
The objective of the invention is to: provide a kind of utilize the liquid nitrogen cryogenics ball milling add in low temperature force the method that worker's technology prepares the ultra-high-strength aluminum alloy material.Help promoting the practical application and the development of China's nano material technology, for its engineering practical application provides advanced material foundation and technological reserve.
Formation of the present invention: select for use to contain the Al-Zn-Mg-Cu alloy of Zn amount greater than 8 weight %, obtain the aluminium alloy powder with induction furnace prealloy ingot and with the aerosolization method, adopt the liquid nitrogen cryogenics ball grinding technique to prepare the nano aluminum alloy powder of high thermal stability then, low temperature is forced worker's technology and is prepared the strong block nanometer aluminum alloy materials of superelevation in utilizing at last; Concrete grammar is as follows:
1, select alloying component:
Alloying component is: 9.5～11.0 weight %Zn, and 2.7～3.2 weight %Mg, 1.7～2.2 weight %Cu, 0.1～0.2 weight %Zr, 0.1～0.2 weight %Ni, all the other are Al.The Al that the present invention selects for use, Zn, Mg, Cu, Zr and Ni are respectively industrial pure Al, technical pure Zn, technical pure Mg, electrolysis Cu, Al-Zr intermediate alloy and Al-Ni intermediate alloy.
2, prealloy ingot preparation: prepare burden by above-mentioned alloying component, utilize induction furnace that alloy material is melted and be heated to 800～850 ℃ of insulations to make its homogenising in 5-15 minute.Be cast into the prealloy ingot after adopting conventional alloy refining degas operation.
3, aerosolization powder process:
Above-mentioned prealloy ingot is put into antivacuum aerosolization equipment.Utilize the intermediate frequency furnace heating, be warming up to 800～850 ℃, produce Al alloy powder after the alloy refining degas operation of employing routine.The aerosolization technological parameter is selected as follows: atomization gas is argon gas or nitrogen, and atomizing pressure is 0.4～0.6MPa, and draft-tube diameter is 3.0～3.5mm.
4, the low temperature ball milling is produced the nano aluminum alloy powder of high thermal stability:
To will greatly influence mechanical milling process in the cryogenic liquid medium adding ball milling environment.Research work shows that the ball milling under the liquid nitrogen temperature causes original position to form the nitrogen oxide of nanoscale.Observed obvious heat endurance is summed up as the pinning effect of these nitrogen oxide particles and foreign atom generation in the low temperature ball-milled powder.
(1) selecting for use of ball mill device: select vertical rotor ball mill or the horizontal rotor ball mill of high energy to carry out ball milling.
(2) ball milling temperature: the temperature of low temperature ball milling liquid nitrogen often is controlled between-110～-160 ℃.Ball milling can make alloyed aluminium variable crisp under lower temperature, helps the fragmentation of particle, obtains less nanocrystalline size.
(3) the ball milling time: the ball milling time is elected 2～12 hours as.
(4) ratio of grinding media to material: ratio of grinding media to material is chosen as 30～50: 1.
5, utilize in low temperature force worker's technology and prepare the strong block nanometer aluminum alloy materials of superelevation:
(1) vacuum hotpressing: vacuum is 10
-2～10
-3Handkerchief, heating-up temperature are 400～550 ℃, and pressure is 200～500MPa.
(2) extruding: temperature is 400～490 ℃, and extrusion ratio is 20～50: 1.
(3) solution treatment: can adopt single-stage solid solution or twin-stage solid solution.When adopting the single-stage solid solution, solid solubility temperature is 475～485 ℃, temperature retention time 3 hours.When adopting the twin-stage solid solution, solid solubility temperature is respectively 445～455 ℃ and 475～485 ℃, temperature retention time was respectively 4.5～5 hours and 50～70 minutes.
(4) timeliness: can adopt single-stage aging or two-stage time effect.When adopting single-stage aging, aging temp is 110～130 ℃, and temperature retention time is 8～24 hours.When adopting two-stage time effect, aging temp is respectively 110～130 ℃ and 170～190 ℃, and temperature retention time was respectively 8～24 hours and 50～70 minutes.
Advantage of the present invention is: (1) is easy to realize the batch process scale, helps industrialization development; (2) equipment is simple, and technical process is controlled easily, and comprehensive preparation cost is lower.
Description of drawings
Fig. 1 is the pattern of atomizing Al-Zn-Mg-Cu alloy powder of the present invention.
Fig. 2 is that the average grain size that formed behind the liquid nitrogen ball milling through 2 hours 15 minutes of the present invention is the Al-Zn-Mg-Cu alloy powder organization chart of 39nm.
Fig. 3 is the block nanometer Al-Zn-Mg-Cu alloy material that obtains through 455 ℃/240MPa/40min vacuum hotpressing of the present invention.
Fig. 4 be of the present invention be 25: 1 Al-Zn-Mg-Cu alloy bar materials after the extruding through 410 ℃, extrusion ratio.
The specific embodiment
Embodiment 1
Alloying component is 9.9 weight %Zn, 2.9 weight %Mg, and 1.9 weight %Cu, 0.1 weight %Zr, 0.1 weight %Ni, all the other are Al.Utilize induction furnace that alloy material is melted and be heated to 810 ℃ of insulations and made its homogenising in 10 minutes.Adopt conventional carbon trichloride and prodan refining degasification, be cast into the prealloy ingot then.Above-mentioned prealloy ingot is put into antivacuum aerosolization equipment.Utilize the intermediate frequency furnace heating and be warming up to 800 ℃, produce Al alloy powder after carbon trichloride that employing is conventional and the prodan refining degasification.Atomization gas is a nitrogen, and atomizing pressure is 0.4MPa, and draft-tube diameter is 3.1mm.
Choose vertical rotor ball mill and stainless steel ball and jar, ratio of grinding media to material is 40: 1, and the ball milling temperature is-120 ℃, and ball milling forms average grain size after 2 hours 15 minutes be the Al alloyed powder of 39nm.Adopt vacuum hot-pressing to obtain block Al-Zn-Mg-Cu alloy material.Vacuum is 10
-3Handkerchief, heating-up temperature are 450 ℃, and pressure is 284MPa.Block Al-Zn-Mg-Cu alloy material average grain size is 68nm.Above-mentioned block materials is squeezed out coupon.Heating-up temperature is 420 ℃, and extrusion ratio is 25: 1.Adopt the single-stage solid solution, solid solubility temperature is 475 ℃, and temperature retention time is 3 hours.Carry out single-stage aging subsequently, aging temp is 120 ℃, and temperature retention time is 24 hours.The coupon ultimate tensile strength is 786MPa, and percentage elongation is 8%.
Embodiment 2
Alloying component is 10.2 weight %Zn, 3.1 weight %Mg, and 1.9 weight %Cu, 0.1 weight %Zr, 0.1 weight %Ni, all the other are Al.Utilize induction furnace that alloy material is melted and be heated to 830 ℃ of insulations and made its homogenising in 10 minutes.Adopt conventional carbon trichloride and prodan refining degasification, be cast into the prealloy ingot then.Above-mentioned prealloy ingot is put into antivacuum aerosolization equipment.Utilize the intermediate frequency furnace heating and be warming up to 820 ℃, produce Al alloy powder after carbon trichloride that employing is conventional and the prodan refining degasification.Atomization gas is a nitrogen, and atomizing pressure is 0.5MPa, and draft-tube diameter is 3.2mm.
Choose vertical rotor ball mill and stainless steel ball and jar, ratio of grinding media to material is 35: 1, and the ball milling temperature is-140 ℃, and ball milling forms the Al alloyed powder that average grain size is 32nm after 7 hours.Adopt vacuum hot-pressing to obtain block Al-Zn-Mg-Cu alloy material.Vacuum is 10
-2Handkerchief, heating-up temperature are 500 ℃, and pressure is 368MPa.Block Al-Zn-Mg-Cu alloy material average grain size is 72nm.Above-mentioned block materials is squeezed out coupon.Heating-up temperature is 450 ℃, and extrusion ratio is 30: 1.Adopt the twin-stage solid solution, solid solubility temperature is respectively 450 ℃ and 480 ℃, temperature retention time was respectively 5 hours and 1 hour.Carry out single-stage aging subsequently, aging temp is 120 ℃, and temperature retention time is 10 hours.The coupon ultimate tensile strength is 860MPa, and percentage elongation is 6%.
Embodiment 3
Alloying component is 10.6 weight %Zn, 2.8 weight %Mg, and 2.0 weight %Cu, 0.2 weight %Zr, 0.2 weight %Ni, all the other are Al.Utilize induction furnace that alloy material is melted and be heated to 840 ℃ of insulations and made its homogenising in 10 minutes.Adopt conventional carbon trichloride and prodan refining degasification, be cast into the prealloy ingot then.Above-mentioned prealloy ingot is put into antivacuum aerosolization equipment.Utilize the intermediate frequency furnace heating and be warming up to 840 ℃, produce Al alloy powder after carbon trichloride that employing is conventional and the prodan refining degasification.Atomization gas is an argon gas, and atomizing pressure is 0.6MPa, and draft-tube diameter is 3.3mm.
Choose horizontal rotor ball mill of high energy and stainless steel ball and jar, ratio of grinding media to material is 50: 1, and the ball milling temperature is-150 ℃, and ball milling forms the Al alloyed powder that average grain size is 29nm after 11 hours.Adopt vacuum hot-pressing to obtain block Al-Zn-Mg-Cu alloy material.Vacuum is 10
-3Handkerchief, heating-up temperature are 550 ℃, and pressure is 500MPa.Block Al-Zn-Mg-Cu alloy material average grain size is 78nm.Above-mentioned block materials is squeezed out coupon.Heating-up temperature is 420 ℃, and extrusion ratio is 50: 1.Adopt the single-stage solid solution, solid solubility temperature is 475 ℃, and temperature retention time is 3 hours.Carry out two-stage time effect subsequently, aging temp is respectively 120 ℃ and 180 ℃, and temperature retention time was respectively 12 hours and 1 hour.The coupon ultimate tensile strength is 910MPa, and percentage elongation is 5%.
Claims (6)
1, a kind of preparation method of superhigh intensity block nanometer aluminium alloy, it is characterized in that: selecting the Al-Zn-Mg-Cu alloy for use is raw material, its alloying component is: 9.5～11.0 weight %Zn, 2.7～3.2 weight %Mg, 1.7～2.2 weight %Cu, 0.1～0.2 weight %Zr, 0.1～0.2 weight %Ni, all the other are Al; With induction furnace prealloy ingot, and obtain the aluminium alloy powder with the aerosolization method, adopt the liquid nitrogen cryogenics ball milling to prepare the nano aluminum alloy powder of high thermal stability then, low temperature is forced worker's technology and is prepared the strong block nanometer aluminum alloy materials of superelevation in utilizing at last.
2, in accordance with the method for claim 1, it is characterized in that: the Al that selects for use, Zn, Mg, Cu, Zr and Ni are respectively industrial pure Al, technical pure Zn, technical pure Mg, electrolysis Cu, Al-Zr intermediate alloy and Al-Ni intermediate alloy.
3, according to claim 1 or 2 described methods, it is characterized in that: described prealloy ingot is meant by above-mentioned alloying component prepares burden, and utilizes induction furnace with alloy material fusing and be heated to 800～850 ℃, is incubated 5-15 minute and makes its homogenising; Be cast into the prealloy ingot after adopting conventional alloy refining degas operation then.
4, according to claim 1 or 2 described methods, it is characterized in that: described is that above-mentioned prealloy ingot is put into antivacuum aerosolization equipment with aerosolization method acquisition aluminium alloy powder, utilize the intermediate frequency furnace heating, be warming up to 800～850 ℃, produce Al alloy powder after the alloy refining degas operation of employing routine; The aerosolization technological parameter is: atomization gas is argon gas or nitrogen, and atomizing pressure is 0.4～0.6MPa, and draft-tube diameter is 3.0～3.5mm.
5, according to claim 1 or 2 described methods, it is characterized in that: the nano aluminum alloy powder technology that described low temperature ball milling is produced high thermal stability is:
Selecting for use of a, ball mill device: select vertical rotor ball mill or the horizontal rotor ball mill of high energy to carry out ball milling;
B, ball milling temperature: the temperature of low temperature ball milling liquid nitrogen is controlled between-110～-160 ℃;
C, ball milling time: the ball milling time is elected 2～12 hours as;
D, ratio of grinding media to material: ratio of grinding media to material is chosen as 30～50: 1.
6, according to claim 1 or 2 described methods, it is characterized in that: low temperature is forced worker's technology and is prepared the technology of the strong block nanometer aluminum alloy materials of superelevation and be in the described utilization:
A, vacuum hotpressing: vacuum is 10
-2～10
-3Handkerchief, heating-up temperature are 400～550 ℃, and pressure is 200～500Mpa;
B, extruding: temperature is 400～490 ℃, and extrusion ratio is 20～50: 1;
C, solution treatment: adopt single-stage solid solution or twin-stage solid solution; When adopting the single-stage solid solution, solid solubility temperature is 475～485 ℃, temperature retention time 3 hours; When adopting the twin-stage solid solution, solid solubility temperature is respectively 445～455 ℃ and 475～485 ℃, temperature retention time was respectively 4.5～5 hours and 50～70 minutes.
D, timeliness: when adopting single-stage aging, aging temp is 110～130 ℃, and temperature retention time is 8～24 hours; When adopting two-stage time effect, aging temp is respectively 110～130 ℃ and 170～190 ℃, and temperature retention time was respectively 8～24 hours and 50～70 minutes.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN200410009661.7A CN1263572C (en) | 2004-10-14 | 2004-10-14 | Method for preparing block of nano aluminum alloy in ultrahigh strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN200410009661.7A CN1263572C (en) | 2004-10-14 | 2004-10-14 | Method for preparing block of nano aluminum alloy in ultrahigh strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1600466A true CN1600466A (en) | 2005-03-30 |
| CN1263572C CN1263572C (en) | 2006-07-12 |
Family
ID=34662562
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200410009661.7A Expired - Fee Related CN1263572C (en) | 2004-10-14 | 2004-10-14 | Method for preparing block of nano aluminum alloy in ultrahigh strength |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1263572C (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102242326A (en) * | 2011-07-01 | 2011-11-16 | 中南大学 | Al-Zn-Mg-Cu aluminum alloy deformation-solid solution heat treatment technology |
| CN103041896A (en) * | 2012-12-28 | 2013-04-17 | 武汉理工大学 | Method for preparing tin antimony oxide nanometer powder in low-temperature ball-milling way |
| CN103394538A (en) * | 2013-08-06 | 2013-11-20 | 浙江瑞金铜铝型材有限公司 | Molding and aging technology of 7A04 superhard aluminum alloy section bar |
| CN105081328A (en) * | 2015-08-05 | 2015-11-25 | 苏州好洁清洁器具有限公司 | Manufacturing method for high-strength aluminum alloy pipe |
| CN105088034A (en) * | 2015-08-05 | 2015-11-25 | 苏州好洁清洁器具有限公司 | High-strength aluminum alloy pipe |
| CN105441705A (en) * | 2015-11-14 | 2016-03-30 | 合肥标兵凯基新型材料有限公司 | Preparation method for high-strength and high-toughness aluminum alloy |
| CN107779795A (en) * | 2016-08-31 | 2018-03-09 | 中南大学 | The double_stage guide heat riser and method of a kind of aluminium alloy thick plate |
| CN107937841A (en) * | 2016-10-12 | 2018-04-20 | 中南大学 | A kind of aluminium alloy single-stage is dissolved the method that is rapidly heated |
-
2004
- 2004-10-14 CN CN200410009661.7A patent/CN1263572C/en not_active Expired - Fee Related
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102242326A (en) * | 2011-07-01 | 2011-11-16 | 中南大学 | Al-Zn-Mg-Cu aluminum alloy deformation-solid solution heat treatment technology |
| CN102242326B (en) * | 2011-07-01 | 2013-04-10 | 中南大学 | Al-Zn-Mg-Cu aluminum alloy deformation-solid solution heat treatment technology |
| CN103041896A (en) * | 2012-12-28 | 2013-04-17 | 武汉理工大学 | Method for preparing tin antimony oxide nanometer powder in low-temperature ball-milling way |
| CN103394538A (en) * | 2013-08-06 | 2013-11-20 | 浙江瑞金铜铝型材有限公司 | Molding and aging technology of 7A04 superhard aluminum alloy section bar |
| CN105081328A (en) * | 2015-08-05 | 2015-11-25 | 苏州好洁清洁器具有限公司 | Manufacturing method for high-strength aluminum alloy pipe |
| CN105088034A (en) * | 2015-08-05 | 2015-11-25 | 苏州好洁清洁器具有限公司 | High-strength aluminum alloy pipe |
| CN105441705A (en) * | 2015-11-14 | 2016-03-30 | 合肥标兵凯基新型材料有限公司 | Preparation method for high-strength and high-toughness aluminum alloy |
| CN107779795A (en) * | 2016-08-31 | 2018-03-09 | 中南大学 | The double_stage guide heat riser and method of a kind of aluminium alloy thick plate |
| CN107937841A (en) * | 2016-10-12 | 2018-04-20 | 中南大学 | A kind of aluminium alloy single-stage is dissolved the method that is rapidly heated |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1263572C (en) | 2006-07-12 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| Ozerov et al. | Evolution of microstructure and mechanical properties of Ti/TiB metal-matrix composite during isothermal multiaxial forging | |
| CN109852834B (en) | Preparation method of nano ceramic particle reinforced metal-based hierarchical configuration composite material | |
| CN1888108A (en) | Cariaceous high-damping deformation magnesium alloy and its prepn process | |
| CN1263572C (en) | Method for preparing block of nano aluminum alloy in ultrahigh strength | |
| CN100432267C (en) | High-strength magnesium based composite material and preparation method thereof | |
| Jiang et al. | In situ formation of TiC–(Ti–6Al–4V) composites | |
| CN114438383A (en) | Multistage intermetallic compound reinforced heat-resistant alloy and preparation method thereof | |
| CN109852859A (en) | High-toughness heat-resistant Mg-Y-Er alloy and preparation method thereof suitable for gravitational casting | |
| CN102230100B (en) | Method for preparing Ti-Nb-Zr-Sn alloy by using powder metallurgical process | |
| CN112063885B (en) | Ruthenium-containing multi-component TiAl alloy suitable for 800 DEG C | |
| CN109182858B (en) | Ho-containing heat-resistant magnesium alloy and preparation method thereof | |
| CN115679141B (en) | Preparation method of layered distribution ceramic reinforced aluminum composite material | |
| CN108359852B (en) | Graphene-reinforced high-silicon aluminum-based composite material and preparation method thereof | |
| CN104018049B (en) | A kind of superplasticity magnesium alloy and preparation method thereof | |
| CN116287913A (en) | Microelement modified aluminum lithium alloy powder for additive manufacturing and preparation method thereof | |
| CN1151299C (en) | Process for preparing Ti-base composition by self reaction and powder metallurgy | |
| CN103966494A (en) | Highly heat-resistant magnalium containing calcium and rare earth | |
| Sheng et al. | Investigation on B, Cr doped Ni3Al alloy prepared by self-propagation high-temperature synthesis and hot extrusion | |
| CN109182806B (en) | Preparation method of ultralight high-strength magnesium-lithium alloy | |
| CN110819860A (en) | Aluminum-copper-manganese porous composite material and preparation method and application thereof | |
| CN115584419B (en) | Heat-resistant biphase magnesium-lithium alloy and preparation method thereof | |
| CN109881065A (en) | High-toughness heat-resistant Mg-Gd-Er alloy and preparation method thereof suitable for low pressure casting | |
| CN103695740A (en) | High-plasticity heat-resistant magnesium alloy | |
| CN1216166C (en) | Preparation of high-strength aluminium alloy | |
| CN116926387B (en) | Heat-resistant high-strength Al-Si alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| EE01 | Entry into force of recordation of patent licensing contract |
Assignee: Hebei Lizhong Group Assignor: University of Science and Technology Beijing Contract fulfillment period: 2007.9.27 to 2012.9.26 contract change Contract record no.: 2008990000560 Denomination of invention: Method for preparing block of nano aluminum alloy in ultrahigh strength Granted publication date: 20060712 License type: Exclusive license Record date: 2008.10.7 |
|
| LIC | Patent licence contract for exploitation submitted for record |
Free format text: EXCLUSIVE LICENSE; TIME LIMIT OF IMPLEMENTING CONTACT: 2007.9.27 TO 2012.9.26; CHANGE OF CONTRACT Name of requester: HEBEI LIZHONG NONFERROUS METAL GROUP CO.,LTD. Effective date: 20081007 |
|
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20060712 Termination date: 20111014 |