CN101343720A - Three-stage solution heat treatment method for Al-Zn-Mg-Cu system aluminum alloy - Google Patents
Three-stage solution heat treatment method for Al-Zn-Mg-Cu system aluminum alloy Download PDFInfo
- Publication number
- CN101343720A CN101343720A CNA2008100321242A CN200810032124A CN101343720A CN 101343720 A CN101343720 A CN 101343720A CN A2008100321242 A CNA2008100321242 A CN A2008100321242A CN 200810032124 A CN200810032124 A CN 200810032124A CN 101343720 A CN101343720 A CN 101343720A
- Authority
- CN
- China
- Prior art keywords
- temperature
- solid solution
- alloy material
- alloy
- insulation
- 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
Abstract
Disclosed is a three-stage solid solution heat treatment method of an Al-Zn-Mg-Cu family aluminum alloy. The Al-Zn-Mg-Cu family aluminum alloy three-stage solid solution heat treatment method comprises the following process steps: the solid solution temperature of the Al-Zn-Mg-Cu family aluminum alloy is between 470 to 490 DEG C, and the temperature is maintained for 1 to 4 hours to realize the solid solution; then, the alloy material temperature is reduced to 380 to 430 DEG C from the alloy material solid solution temperature at a cooling rate of 0.5 to 1.5 DEG C per minute, the alloy temperature is reduced and the precipitation is performed; thereafter, the temperature is increased to 450 to 480 DEG C at a cooling rate of 5 to 10 DEG C per minute, the temperature is maintained for 2 to 10 minutes, the alloy is taken from the furnace for water quenching. The invention has the advantages that the process method is simple, the operation is convenient, and when the alloy strength is retained, the corrosion resistance performance is enhanced, continuous operation is realizable, the method is suitable for industrial production, and can replace the existing Al-Zn-Mg-Cu family aluminum alloy enforced heat treatment method, and the aluminum alloy application field is widened.
Description
Technical field
The present invention relates to a kind of heat treating method of the Al-Zn-Mg-Cu of improvement line aluminium alloy corrosion resistance, be meant a kind of three-stage solution heat treatment method of Al-Zn-Mg-Cu line aluminium alloy especially.The aluminum alloy heat treatment process that belongs to field of metallurgy.
Background technology
The AI-Zn-Mg-Cu line aluminium alloy is a kind of heat-treatable strengthened high strength alumin ium alloy, utilizes quench aging technology can improve the intensity of alloy.But precipitated phase enrichment on the crystal boundary is continuous distribution in ag(e)ing process, reduces the toughness and the corrosion resistance of alloy.Be toughness and the corrosion resistance that improves alloy, people regulate intracrystalline and crystal boundary precipitated phase distribution mainly by multistage aging technology.Adopt the two-stage time effect process [Central South University's journal (natural science edition), 2007,38 the 6th phases of volume, P1045.] of peak timeliness+overaging, wherein first step timeliness is the low temperature preageing, is equivalent to nucleation stage, forms a large amount of GP districts.Those can the preferential nucleation in GP district of stable existence be converted into η ' phase under the high-temperature aging temperature.The second stage is high-temperature aging, makes η ' phase and η particle gathering mutually, nodularization on the crystal boundary, thereby destroys the continuity of crystal boundary precipitated phase, improves the toughness and the corrosion resistance of alloy, and particularly the anti-stress corrosion performance to alloy has clear improvement.But when the timeliness of the second stage, alligatoring has taken place in the particle of intracrystalline precipitated phase, and therefore, this institution of prescription improves over-all properties with sacrificial alloy material certain intensity.For solving the contradiction between intensity and the corrosion resistance, Cina proposes three grades of aging technique [US Patent No-4477292 of regression and re-ageing; MetallurgicalTransactions, 1984, Vols.15A, P1531], this aging technique is the high temperature regression treatment that adds the short period of time after the peak value timeliness, and then carries out the peak value ageing treatment.After complete regression and re-ageing processing, crystal grain inside forms as the precipitated phase of peak value timeliness state and obtains maximum strength, and the tissue of the similar overaging state of formation on the crystal boundary so just makes alloy when keeping peak timeliness intensity, and corrosion resistance also can be near the two-stage time effect level.But there are problems such as technology is long, the temperature regulation window is less in three grades of aging techniques, are very restricted in practical application in industry.
The present inventor once proposed to separate out processing in advance by high temperature, promptly handle in the solid solubility temperature insulation earlier, reduce temperature (than low 20～30 ℃ of solid solubility temperature) and short period of time insulation subsequently, quench then and timeliness, separate out the precipitation state of regulation and control crystal boundary by high temperature in advance, make crystal boundary precipitated phase alligatoring in the alloy, plastisied dispersion increases, and regulates the current potential between crystal boundary and the intracrystalline, thereby improves corrosion resistance [Rare Metals Materials and the engineering of alloy, 2007 36 the 9th phases of volume, P1628; Scripta Materialia, 2007, vols 56, P305].But high temperature is separated out the limitation that also there is its application in processing in advance, when promptly under nearly solid solubility temperature, separating out, can suppress alloy material separating out at intracrystalline, guarantee the ageing strengthening effect of alloy material, but under this temperature alloy material on crystal boundary separate out and insufficient, crystal boundary precipitated phase particle is very discrete, and limited amount.In ag(e)ing process subsequently, less on the crystal boundary as the particle of timeliness precipitated phase forming core core, crystal boundary enough big forming core motivating force will be impelled timeliness precipitated phase spontaneous nucleation and be continuous distribution and separate out in these grain spacing this moment, so unsatisfactory to the improvement of alloy material corrosion resistance.And when under low temperature more, separating out in advance, the number of precipitated phase of state of being in a discrete distribution on the crystal boundary will further increase, but the forming core motivating force is enough at the intracrystalline forming core, and also will have even tiny precipitated phase to separate out at the alloy material intracrystalline this moment, reduce the saturated solid solubility of alloy material to a certain extent.Therefore, reduce that to separate out that temperature separates out be to improve its corrosion resistance on the certain intensity based of sacrificial alloy material.High temperature is separated out in advance in actual applications and can be brought new problem in addition, promptly in process of production, the quenching of alloy material needs transfer time, in the quenching transfer process, the temperature on alloy material top layer will further reduce on the basis of separating out temperature in advance, this makes the intracrystalline on alloy material top layer and crystal boundary separate out more precipitated phase, further reduces the degree of supersaturation of alloy material top layer sosoloid, finally influences its timeliness strengthening effect.
Summary of the invention
The objective of the invention is to overcome the deficiency of prior art and provide that but a kind of processing method is simple, easy to operate, the three-stage solution heat treatment method of the Al-Zn-Mg-Cu line aluminium alloy of the operate continuously that improves its corrosion resistance when keeping alloy material intensity.
The present invention--the three-stage solution heat treatment method of-a kind of Al-Zn-Mg-Cu line aluminium alloy comprises following processing step:
1) solid solution: in 470～490 ℃ of solid solubility temperatures, insulation 1～4h realizes solid solution with the Al-Zn-Mg-Cu line aluminium alloy.
2) cooling is separated out: from the alloy material solid solubility temperature, make alloy material cool to 380～430 ℃ with the rate of temperature fall of 0.5～1.5 ℃/min, insulation 0.5～10h.
3) solid solution again: after end is separated out in cooling, make alloy material be warmed up to 450～480 ℃ with the temperature rise rate of 5～10 ℃/min, insulation 2～10min comes out of the stove shrend.
A kind of three-stage solution heat treatment method of Al-Zn-Mg-Cu line aluminium alloy comprises following processing step:
1) solid solution: in 475～485 ℃ of solid solubility temperatures, insulation 1.5～3.5h realizes solid solution with the Al-Zn-Mg-Cu line aluminium alloy.
2) cooling is separated out: from the alloy material solid solubility temperature, make alloy material cool to 390～420 ℃ with the rate of temperature fall of 0.8～1.2 ℃/min, insulation 3.5～7h.
3) solid solution again: after end is separated out in cooling, make alloy material be warmed up to 460～470 ℃ with the temperature rise rate of 6～8 ℃/min, insulation 4～8min comes out of the stove shrend.
A kind of three-stage solution heat treatment method of Al-Zn-Mg-Cu line aluminium alloy comprises following processing step:
1) solid solution: in 480 ℃ of solid solubility temperatures, insulation 2h realizes solid solution with the Al-Zn-Mg-Cu line aluminium alloy.
2) cooling is separated out: from the alloy material solid solubility temperature, make alloy material cool to 410 ℃ with the rate of temperature fall of 1.0 ℃/min, insulation 5h.
3) solid solution again: after end is separated out in cooling, make alloy material be warmed up to 465 ℃ with the temperature rise rate of 7 ℃/min, insulation 6min comes out of the stove shrend.
The present invention by a solid solution, improves main alloying element and impurity element solid solution degree in matrix owing to adopt above-mentioned processing method to greatest extent; Subsequently, separate out, alloy is fully separated out on crystal boundary, and form the big and discrete precipitated phase that distributes of particle, then separate out the tiny precipitated phase of small quantities of particles at intracrystalline by cooling; Separate out by solid solution-cooling, quantity, size and the distribution of crystal boundary and intracrystalline precipitated phase in the regulation and control alloy make alloy form the big and discrete precipitated phase that distributes of particle on crystal boundary, and at intracrystalline formation is evenly distributed, particle is tiny precipitated phase.At last, alloy material is warmed up to solid solubility temperature once more carries out solid solution in short-term, its effect comprises following two aspects: on the one hand, make the tiny precipitated phase solid solution again of intracrystalline in the alloy material, the big precipitated phase that is discontinuous distribution on the crystal boundary is then because of coming not anxious solid solution to be kept.Handle by the quench aging of carrying out subsequently, the precipitated phase particle that is discontinuous distribution in a large number that keeps in the solid solution process on the crystal boundary will be as the forming core core of timeliness precipitated phase, make that the precipitated phase structure still keeps discontinuous distribution on the crystal boundary, thereby alloy material is obtained than better corrosion resistance after general solid solution and corresponding timeliness, keeping crystal boundary to separate out effect in advance like this, when improving the alloy material corrosion resistance, also can avoid because of cooling separate out and subsequently quenching transfer process in precipitated phase separating out in a large number in alloy material inside, guarantee that alloy material obtains sufficiently high saturated solid solubility, the ageing strengthening after not influencing it and quenching.。On the other hand, can improve the quenching temperature of alloy material, avoid its in the quenching transfer process further cooling separate out, make alloy material obtain corresponding saturated solid solubility, to guarantee its ageing strengthening effect after quenching.In addition, solid solution-cooling separates out-again solid solution three-stage solution thermal treatment process regulation and control crystal boundary to separate out be to finish in solid solution stage at alloy material, and the processing in each stage can operation in same heat treatment furnace, so the operate continuously of technology of the present invention makes it suitable to industrial production.In sum, processing method of the present invention is simple, easy to operate, improve its corrosion resistance when keeping alloy material intensity, but operate continuously is suitable for industrialized production, alternative existing Al-Zn-Mg-Cu is the alloy strengthening thermal treatment process, enlarges the Application Areas of aluminium alloy.
Embodiment
For implementing the present invention, adopting the Al-Zn-Mg-Cu that belongs to heterogeneity is that alloy is tested.Embodiment all adopts semicontinuous casting with sample, handles through the classification homogenizing then.The sample deformation process adopts the high temperature forging and pressing, 400 ℃～430 ℃ of forging and pressing temperature, the forging and pressing deflection is controlled to be 80%, after the sample after the forging and pressing adopts the three-stage solution art breading, adopt peak value or three grades of timeliness, and separate out in advance to handle with single-stage solution treatment and high temperature and compare.The laboratory sample result detects and adopts hardness, specific conductivity test and peel off the corrosion class evaluation, wherein peels off corrosion (EXCO) experiment and carries out with reference to U.S. ASTM-G34-1979 standard, and it is NaCl 4.0mol/L that standard EXCO degrades solution ratio, KNO
30.5mol/L and HNO
30.1mol/L surplus is distilled water (or deionized water), experimental temperature is constant to be (25 ± 2) ℃, and the corrosive medium volume is 20ml: 1cm with the ratio of erosional surface area
2Sample is flooded 48h in solution, in 0～24h, uninterruptedly observe rating, and carry out photographic recording with metaloscope.Behind the 48h sample is taken out direct survey sample and rating when dampness, water flushing sample soaks 2～3min and removes corrosion product in 30% salpeter solution then, again through washing, drying up.
Embodiment 1:
The technic metal chemical ingredients is: Al-6.5Zn-2.4Mg-2.2Cu-0.13Zr (massfraction).Conventional solution treatment is adopted in solid solution, i.e. directly shrend behind 480 ℃ of insulation 3h.Quenching is less than 5s transfer time, adopt the peak value timeliness (130 ℃/24h) and three grades of timeliness (130 ℃/24h → 180 ℃/1h → 130 ℃/24h) dual mode carries out timeliness.Carry out the test of hardness and specific conductivity behind the completion of prescription, experimental result is as shown in table 1.Subsequently the peak value aging samples is peeled off the corrosion class evaluation.Evaluation result is as shown in table 3.
Embodiment 2:
The technic metal chemical ingredients is: Al-6.5Zn-2.4Mg-2.2Cu-0.13Zr (massfraction).Solution treatment adopts three-stage solution thermal treatment and high temperature to separate out the technology contrast in advance:
(1) three-stage solution thermal treatment: sample directly is warming up to 470 ℃ of insulation 1h, cools to 380 ℃ and be incubated 0.5h with the speed of 0.5 ℃/min subsequently, and the speed with 5 ℃/min is warmed up to 450 ℃ again, insulation 2min.
(2) solid solution-cooling is separated out (low temperature is separated out) and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 420 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
(3) high temperature is separated out (high temperature is separated out) in advance and handled: the fs is adopted the processing mode identical with the three-stage solution thermal treatment fs, cools to 455 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
All samples carries out shrend immediately after solution treatment, all be less than 5 seconds the transfer time of quenching, all adopt subsequently the peak value timeliness (130 ℃/24h) and three grades of timeliness (130 ℃/24h → 180 ℃/1h → 30 ℃/24h) dual mode is handled.Carry out the test of hardness and specific conductivity behind the completion of prescription, experimental result is as shown in table 1.Subsequently the peak value aging samples of (1) and (3) solid solution condition is peeled off the corrosion class evaluation, evaluation result is as shown in table 3.
Embodiment 3:
The technic metal chemical ingredients is: Al-8.6Zn-2.5Mg-2.2Cu-0.16Zr (massfraction).Solution treatment adopts three-stage solution thermal treatment and high temperature to separate out the technology contrast in advance, concrete implementing process:
(1) three-stage solution thermal treatment: be warming up to 480 ℃ and be incubated 2h with stove, cool to 400 ℃ and be incubated 5h with the speed of 1 ℃/min subsequently, the speed with 5 ℃/min is warmed up to 470 ℃ again, and soaking time is 5min.
(2) solid solution-cooling is separated out (low temperature is separated out) and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 430 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
(3) high temperature is separated out (high temperature is separated out) in advance and handled: the fs is adopted the processing mode identical with the three-stage solution thermal treatment fs, cools to 460 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
All samples carries out shrend immediately after solution treatment, all be less than 5 seconds the transfer time of quenching, every kind of technology all adopt the peak value timeliness (130 ℃/24h) and three grades of timeliness (130 ℃/24h → 180 ℃/1h → 130 ℃/24h) dual mode is handled.Carry out the test of hardness and specific conductivity behind the completion of prescription, experimental result is as shown in table 1.
Embodiment 4:
The technic metal chemical ingredients is: Al-8.4Zn-2.4Mg-2.6Cu-0.22Zr (massfraction).Solution treatment adopts three-stage solution thermal treatment and high temperature to separate out the technology contrast in advance, concrete implementing process:
(1) three-stage solution thermal treatment: be warming up to 490 ℃ of insulation 4h with stove, cool to 430 ℃ and be incubated 10h with the speed of 1.5 ℃/min subsequently, the speed with 10 ℃/min is warmed up to 480 ℃ again, insulation 10min.
(2) solid solution-cooling is separated out (low temperature is separated out) and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 400 ℃ and be incubated 30min with the speed of 1 ℃/min subsequently.
(3) high temperature is separated out (high temperature is separated out) in advance and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 465 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
All samples carries out shrend immediately after solution treatment, all be less than 5 seconds the transfer time of quenching, every kind of technology all adopt the peak value timeliness (130 ℃/24h) and three grades of timeliness (130 ℃/24h → 180 ℃/1h → 130 ℃/24h) dual mode is handled.Carry out the test of hardness and specific conductivity behind the completion of prescription, experimental result is as shown in table 1.
Embodiment 5:
The technic metal chemical ingredients is: Al-4.4Zn-2.4Mg-0.13Cu-0.12Zr-0.24Mn-0.13Cr (massfraction).Solution treatment adopts three-stage solution thermal treatment and high temperature to separate out the technology contrast in advance, concrete implementing process:
(1) three-stage solution thermal treatment: be warming up to 470 ℃ and be incubated 4h with stove, cool to 380 ℃ and be incubated 2h with the speed of 1.5 ℃/min subsequently, the speed with 10 ℃/min is warmed up to 450 ℃ again, and soaking time is 5min.
(2) solid solution-cooling is separated out (low temperature is separated out) and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 380 ℃ and be incubated 30min with the speed of 1 ℃/min subsequently.
(3) high temperature is separated out (high temperature is separated out) in advance and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 450 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently
All samples carries out shrend immediately after solution treatment, all be less than 5 seconds the transfer time of quenching, every kind of technology all adopt the peak value timeliness (120 ℃/24h) and three grades of timeliness (120 ℃/24h → 170 ℃/1h → 120 ℃/24h) dual mode is handled.Carry out the test of hardness and specific conductivity behind the completion of prescription, experimental result is as shown in table 1.
Embodiment 6:
The technic metal chemical ingredients is: Al-6.5Zn-2.4Mg-2.2Cu-0.13Zr (massfraction).Solution treatment adopts three-stage solution thermal treatment and high temperature to separate out the technology contrast in advance:
(1) three-stage solution thermal treatment: sample directly is warming up to 480 ℃ and be incubated 2h, cools to 420 ℃ and be incubated 1h with the speed of 0.5 ℃/min subsequently, and the speed with 5 ℃/min is warmed up to 470 ℃ again, insulation 2min.
(2) solid solution-cooling is separated out (low temperature is separated out) and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 420 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
(3) high temperature is separated out (high temperature is separated out) in advance and is handled: the fs adopt with three-stage solution thermal treatment in identical processing mode of fs, cool to 455 ℃ and be incubated 30min with the speed of 0.5 ℃/min subsequently.
All samples does not carry out shrend immediately after solution treatment, controlling the transfer time of quenching is 15 seconds, adopts (130 ℃/24h) handle of peak value timeliness subsequently.Carry out the test of hardness and specific conductivity behind the completion of prescription, experimental result is as shown in table 3.Listing example 2 peak value timeliness results in the table 3 simultaneously in compares.
Table 1 is that four kinds of alloys are handled and Rockwell hardness after timeliness and specific conductivity through different solid solution crafts, table 2 for alloy material through difference quench the residence time after handling Rockwell hardness and specific conductivity (sample all adopt the peak value timeliness (130 ℃/24h), the unified thick thin plate of 5mm that adopts of sample), show from the result of table 1, table 2, adopt three-stage solution heat treatment method of the present invention, through the specific conductivity (%IACS) of peak value ageing treatment sample and hardness (HRB) almost with separate out (height is separated out temperature) or single-stage solid solution in advance through high temperature after three grades of ageing treatment sample quite.As seen, after three-stage solution thermal treatment, alloy material adopts simple peak value timeliness that its corrosion resistance is improved significantly.Table 3 for alloy adopts after different solid solution crafts handle exfoliation Corrosion (sample all adopt the peak value timeliness (130 ℃/24h), experimental data shows in the table 3, and the solution treatment again in the three-stage solution thermal treatment process can effectively solve high temperature and separate out the quenching that exists in advance shift the problem of separating out in production application.
Table 1
Table 2
Table 3
In the table 3:
The N-patterned surface allows variable color or corrosion, but the sign that does not have spot corrosion and degrade.
The P-spot corrosion, discontinuous hot spot has slightly and heaves at the edge of point.
E
A～E
D-peel off the corrosive grade, wherein+that number expression is in the extent of corrosion of this grade is comparatively serious.
E
AThe a small amount of bubbling cracking in-surface is thin slice or powder, and slight stripping layer is arranged.
E
B-tangible layering is arranged and expand to metal inside.
E
C-corrosion expands to darker metal inside.
E
D-corrosion expands to compares E
CDarker metal inside, and have a large amount of metal levels to peel off.
Claims (3)
1, a kind of three-stage solution heat treatment method of Al-Zn-Mg-Cu line aluminium alloy comprises following processing step:
1) solid solution: in 470～490 ℃ of solid solubility temperatures, insulation 1～4h realizes solid solution with the Al-Zn-Mg-Cu line aluminium alloy.
2) cooling is separated out: from the alloy material solid solubility temperature, make alloy material cool to 380～430 ℃ with the rate of temperature fall of 0.5～1.5 ℃/min, insulation 0.5～10h.
3) solid solution again: after end is separated out in cooling, make alloy material be warmed up to 450～480 ℃ with the temperature rise rate of 5～10 ℃/min, insulation 2～10min comes out of the stove shrend.
2, the three-stage solution heat treatment method of a kind of Al-Zn-Mg-Cu line aluminium alloy according to claim 1 comprises following processing step:
1) solid solution: in 475～485 ℃ of solid solubility temperatures, insulation 1.5～3.5h realizes solid solution with the Al-Zn-Mg-Cu line aluminium alloy.
2) cooling is separated out: from the alloy material solid solubility temperature, make alloy material cool to 390～420 ℃ with the rate of temperature fall of 0.8～1.2 ℃/min, insulation 3.5～7h.
3) solid solution again: after end is separated out in cooling, make alloy material be warmed up to 460～470 ℃ with the temperature rise rate of 6～8 ℃/min, insulation 4～8min comes out of the stove shrend.
3, the three-stage solution heat treatment method of a kind of Al-Zn-Mg-Cu line aluminium alloy according to claim 1 comprises following processing step:
1) solid solution: in 480 ℃ of solid solubility temperatures, insulation 2h realizes solid solution with the Al-Zn-Mg-Cu line aluminium alloy.
2) cooling is separated out: from the alloy material solid solubility temperature, make alloy material cool to 410 ℃ with the rate of temperature fall of 1.0 ℃/min, insulation 5h.
3) solid solution again: after end is separated out in cooling, make alloy material be warmed up to 465 ℃ with the temperature rise rate of 7 ℃/min, insulation 6min comes out of the stove shrend.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN200810032124A CN100580129C (en) | 2008-08-22 | 2008-08-22 | Three-stage solution heat treatment method for Al-Zn-Mg-Cu system aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN200810032124A CN100580129C (en) | 2008-08-22 | 2008-08-22 | Three-stage solution heat treatment method for Al-Zn-Mg-Cu system aluminum alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101343720A true CN101343720A (en) | 2009-01-14 |
| CN100580129C CN100580129C (en) | 2010-01-13 |
Family
ID=40245832
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200810032124A Expired - Fee Related CN100580129C (en) | 2008-08-22 | 2008-08-22 | Three-stage solution heat treatment method for Al-Zn-Mg-Cu system aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100580129C (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102268620A (en) * | 2011-08-01 | 2011-12-07 | 南昌大学 | Solid-solution treatment method of Al3Ti particle reinforced Al-Zn-Mg-Cu based aluminum alloys |
| CN102888575A (en) * | 2012-10-22 | 2013-01-23 | 中南大学 | Thermal treatment method for simultaneously improving strength and fatigue resistance property of aluminum alloy |
| CN104451480A (en) * | 2014-12-15 | 2015-03-25 | 西南铝业（集团）有限责任公司 | Solid solution quenching method for aluminum alloy plates |
| CN105734466A (en) * | 2014-12-09 | 2016-07-06 | 北京有色金属研究总院 | Solid solution heat treatment method for improving structure and performance of 7xxx wrought aluminum alloy |
| CN105861968A (en) * | 2016-03-30 | 2016-08-17 | 中南大学 | Method for improving mechanical property of Al-Cu-series high-strength aluminum alloy ring pieces |
| CN109252076A (en) * | 2018-11-13 | 2019-01-22 | 中南大学 | A kind of anticorrosion stress-resistant Al-Zn-Mg- (Cu) alloy and preparation method thereof containing Ta |
| CN113278900A (en) * | 2020-02-20 | 2021-08-20 | 核工业理化工程研究院 | Solid solution treatment method of Al-Zn-Mg-Cu series high-strength aluminum alloy |
| CN114836659A (en) * | 2022-04-25 | 2022-08-02 | 南京工程学院 | Method for improving alloy performance by adding Sc into Al-Cu alloy, material and application |
| CN115074585A (en) * | 2022-06-14 | 2022-09-20 | 三峡大学 | Heat treatment process of Al-Zn-Mg-Cu alloy material |
| CN115927982A (en) * | 2022-11-15 | 2023-04-07 | 福建祥鑫新材料科技有限公司 | Heat treatment method for improving corrosion performance of 7-series aluminum alloy |
| CN117535603A (en) * | 2023-11-07 | 2024-02-09 | 武汉商学院 | Heat treatment method for improving corrosion resistance of 7xxx aluminum alloy |
-
2008
- 2008-08-22 CN CN200810032124A patent/CN100580129C/en not_active Expired - Fee Related
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102268620A (en) * | 2011-08-01 | 2011-12-07 | 南昌大学 | Solid-solution treatment method of Al3Ti particle reinforced Al-Zn-Mg-Cu based aluminum alloys |
| CN102888575A (en) * | 2012-10-22 | 2013-01-23 | 中南大学 | Thermal treatment method for simultaneously improving strength and fatigue resistance property of aluminum alloy |
| CN105734466A (en) * | 2014-12-09 | 2016-07-06 | 北京有色金属研究总院 | Solid solution heat treatment method for improving structure and performance of 7xxx wrought aluminum alloy |
| CN105734466B (en) * | 2014-12-09 | 2017-10-27 | 北京有色金属研究总院 | A kind of solid solution heat treatment method of improvement 7xxx systems wrought aluminium alloy microstructure and property |
| CN104451480A (en) * | 2014-12-15 | 2015-03-25 | 西南铝业（集团）有限责任公司 | Solid solution quenching method for aluminum alloy plates |
| CN105861968A (en) * | 2016-03-30 | 2016-08-17 | 中南大学 | Method for improving mechanical property of Al-Cu-series high-strength aluminum alloy ring pieces |
| CN109252076A (en) * | 2018-11-13 | 2019-01-22 | 中南大学 | A kind of anticorrosion stress-resistant Al-Zn-Mg- (Cu) alloy and preparation method thereof containing Ta |
| CN109252076B (en) * | 2018-11-13 | 2020-10-27 | 中南大学 | Ta-containing stress corrosion resistant Al-Zn-Mg- (Cu) alloy and preparation method thereof |
| CN113278900A (en) * | 2020-02-20 | 2021-08-20 | 核工业理化工程研究院 | Solid solution treatment method of Al-Zn-Mg-Cu series high-strength aluminum alloy |
| CN113278900B (en) * | 2020-02-20 | 2022-05-06 | 核工业理化工程研究院 | Solid solution treatment method of Al-Zn-Mg-Cu series high-strength aluminum alloy |
| CN114836659A (en) * | 2022-04-25 | 2022-08-02 | 南京工程学院 | Method for improving alloy performance by adding Sc into Al-Cu alloy, material and application |
| CN115074585A (en) * | 2022-06-14 | 2022-09-20 | 三峡大学 | Heat treatment process of Al-Zn-Mg-Cu alloy material |
| CN115927982A (en) * | 2022-11-15 | 2023-04-07 | 福建祥鑫新材料科技有限公司 | Heat treatment method for improving corrosion performance of 7-series aluminum alloy |
| CN115927982B (en) * | 2022-11-15 | 2024-04-19 | 福建祥鑫新材料科技有限公司 | Heat treatment method for improving corrosion performance of 7-series aluminum alloy |
| CN117535603A (en) * | 2023-11-07 | 2024-02-09 | 武汉商学院 | Heat treatment method for improving corrosion resistance of 7xxx aluminum alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100580129C (en) | 2010-01-13 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100580129C (en) | Three-stage solution heat treatment method for Al-Zn-Mg-Cu system aluminum alloy | |
| CN101792891B (en) | Aging treatment process of Al-Zn-Mg-Cu aluminum alloy | |
| CN104004947B (en) | High anti intercrystalline corrosion aluminium alloy of 600-650MPa intensity and preparation method thereof | |
| CN101724797B (en) | Solid solution heat treatment method of Al-Zn-Mg-Cu alloy and aluminum alloy treated by using same | |
| CN103602865B (en) | Copper-containing heat-resistant magnesium-tin alloy and preparation method thereof | |
| CN104004946B (en) | 690-730MPa superstrength 80-100mm hardening capacity aluminium alloy and preparation method thereof | |
| CN108165853B (en) | Magnesium alloy with high electromagnetic shielding efficiency and preparation method thereof | |
| CN103695743A (en) | Magnesium alloy and preparation method thereof | |
| CN105018812A (en) | Heat-resistant magnesium alloy and fabrication method thereof | |
| CN101886186B (en) | High temperature shape memory copper alloy and preparation method thereof | |
| CN104694858A (en) | Hot working method capable of simultaneously improving electrical conductivity and strength of aluminum alloy | |
| CN101886187B (en) | Shape memory copper alloy and preparation method thereof | |
| CN105586521A (en) | Mg-Zn-Mn wrought magnesium alloy with high thermal conductivity and preparation method thereof | |
| CN105316550A (en) | High-damping magnesium alloy containing long-periodic structural phase and preparation method for high-damping magnesium alloy | |
| CN112251627A (en) | High-strength high-conductivity Cu-Sc alloy and preparation method thereof | |
| Zhang et al. | Effect of Ti on microstructure and mechanical properties of die-cast Al-Mg-Zn-Si alloy | |
| CN111519057A (en) | Method for prolonging service life of die for preparing aluminum alloy | |
| CN109628779B (en) | Method for refining eutectic phase of Mg-Al-Zn magnesium alloy with high alloy content | |
| CN112226636A (en) | Preparation method of high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate | |
| CN105568190A (en) | Two-stage aging process of Al-5.6Zn-2.1Mg-1.2Cu-0.1Zr-0.1Er alloy | |
| CN103225049A (en) | Treatment process for improving electric conductivity of medium strength aluminium alloy | |
| CN106834806A (en) | A kind of anti-corrosion kirsite and preparation method thereof | |
| CN114411024A (en) | Slab ingot for anodic oxidation 5xxx series aluminum material and preparation method thereof | |
| CN109385561B (en) | Production process of Al-Mg-Si-Zr aluminum alloy tubular bus | |
| CN103173700A (en) | Preparation method of surface deintercalation layer of Al-Cu-Li-X aluminium-lithium alloy |
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 | ||
| C17 | Cessation of patent right | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20100113 Termination date: 20100822 |