CN108265246A - A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches - Google Patents
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches Download PDFInfo
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- CN108265246A CN108265246A CN201810071578.4A CN201810071578A CN108265246A CN 108265246 A CN108265246 A CN 108265246A CN 201810071578 A CN201810071578 A CN 201810071578A CN 108265246 A CN108265246 A CN 108265246A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
Abstract
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, belong to preparation and the technical field of heat treatment of metal and alloy, this method is that the cold rolling pre-treatment of total deformation >=10% is carried out to solution hardening treated aluminium alloy thick plate, then, carry out artificial aging processing, under the premise of alloy surface hardness is not significantly reduced, precipitating reinforcing effect of the alloy under quenching condition at a slow speed is substantially improved, the aging strength of alloy center portion as-quenched at a slow speed is promoted, so as to improve large-sized aluminium alloy component surface and the difference of center portion performance.The present invention only adds one of processing process, easy to operate with regard to that can significantly reduce alloy intensity non-uniformity as caused by quenching, applied widely, and to being used for 7xxx aluminium alloys, centre hardness promotes 30% compared with conventional method.Making the intensity of alloy, overall performance is promoted in the case where meeting service condition.Expand the application field of 7xxx aluminium alloys.
Description
Technical field
The invention discloses a kind of methods for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches, and belong to metal
And preparation and the technical field of heat treatment of alloy.
Background technology
7xxx line aluminium alloys have the intensity of superelevation and good plasticity, toughness, anti-stress corrosion performance, generally as
Structural member is widely used in aerospace and field of track traffic.
The structural member of modern manufacturing tends to enlargement and integration development, tradition to be replaced to be closed by a variety of different aluminums
The combined type component that the assembly of golden ingredient forms, so as to further reach safety and light-weighted requirement.However as
The increase for the structural member size that maximizes, big thickness product often show higher quenching sensitive in quenching process.Mesh
Preceding such as 7050,7055,7075 etc. alloys of common 7xxx aluminium alloys, thickness be more than 120mm after, can all show surface with
The problem of performance difference of center portion is larger, it is difficult to meet the needs of practical application.
For aluminum alloy quenching sensitive question, the prior art is typically by improving the ingredient of alloy, for example improve Zn/
Mg atomic ratios reduce Cu constituent contents or add the method for the trace element such as Zr, Er to drop low-alloyed quenching sensitive
[CN102703782A, a kind of strong high-hardenability Al-Zn-Mg-Cu alloy of superelevation, 2012], [CN103266245B, one kind is low to quench
Fiery sensibility Al-Zn-Mg-Cu series alloys, 2016], [CN107245616A, a kind of 600MPa grades of low-quenching sensitive surpass
High strength alumin ium alloy and preparation method thereof, 2017], also have been reported that and caused by improving quenching apparatus to reach reduction alloy by quenching
Intensity non-uniformity purpose [CN105441835A, a kind of device of high quenching sensitive aluminum alloy squeeze wood press quenching
And method, 2015] or using the method for changing subsequent aging technique, there is no inherently improve alloy to this method
To the sensibility of quenching rate, but center portion is improved by improving precipitating reinforcing effect of the alloy under quenching rate at a slow speed
Intensity, so as to reduce difference [Liu S, Li C, Han S, the Deng Y, Zhang of large scale sample surfaces and center portion performance
X.Effect of natural aging on quench-induced inhomogeneity of microstructure
and hardness in high strength 7055 aluminum alloy.Journal of Alloys&Compounds
2015；625:34.].
These methods all achieve certain achievement, but there is also certain limitations.Such as by improving alloying component,
Design successfully and it is commercial be with 7085,7081 alloy for representative, on ingredient, these alloys improve the content of Zn, reduce
The content of Mg and Cu, while also have adjustment to Trace Zr, but since Mg contents are relatively low, with the business such as 7050,7075
Alloy is compared, and strength character has no advantage, can not also replace 7050 this kind of alloys comprehensively, and is designed new alloy and answered to business
With the work for being also a complexity and costliness；It improves quenching apparatus and can effectively improve intensity non-uniformity caused by quenching, however
The scope of application of this method is smaller, is generally only applicable to extrudate；Although by the method energy for changing follow-up institution of prescription
The enough hardness for improving alloy to a certain extent at a slow speed under quenching condition, for example long-time natrual ageing is introduced, but document report
The natural aging time in road needs [Liu S, Li C, Han S, Deng Y, Zhang X.Effect more than 17820 hours (2 years)
of natural aging on quench-induced inhomogeneity of microstructure and
hardness in high strength 7055 aluminum alloy.Journal of Alloys&Compounds
2015；625:34.], do not meet industrial demand yet.
Pre-treatment is introduced to aluminium alloy, changes the pick-up behavior of follow-up aged, so as to obtain dislocation strengthening with
The resultant effect of precipitation strength improves the intensity of alloy, is a kind of basic deformation heat treatment method, for Al-Cu-Mg with
And Al-Mg-Si alloy can significantly improve its mechanical property [zhong LH, mei LR, peng LX, DENG M, juan LH,
HUANG L.Effect of pre-deformation on microstructures and mechanical
properties of high purity Al–Cu–Mg alloy.Transactions of Nonferrous Metals
Society of China 2016；26:1482],[H LC,L LX,H WS,H CJ,Q T,J C,Y G.A tuning
nano-precipitation approach for achieving enhanced strength and good
ductility in Al alloys.Materials&Design 2014；54:144].But 7xxx alloys are introduced pre-
Deformation process its performance boost often unobvious, having document report to introduce predeformation in 7xxx alloys can cause under its intensity
Drop, mainly since the dislocation of predeformation causes precipitated phase to occur to be roughened [Yin Zhimin, Jiang Rongrong, Lee in follow-up ag(e)ing process
Build Hunan, Yang Zhibing, bravely the influence aluminium of aging state HS755 alloy structures and performance is processed in precooling stretcher strain to woods after strong solid solutions
2009:8.],[lin NA,yi LZ,min ZS.Effect of large cold deformation after solution
treatment on precipitation characteristic and deformation strengthening of
2024 and 7A04 aluminum alloys.Transactions of Nonferrous Metals Society of
China 2006；16:1341].
The prior art is all built upon the aluminium alloy based on complete water cooling state about the research of predeformation, and there is no through hardening
Property the problem of, so far not about for introducing the phase that is influenced on alloy property of predeformation under 7xxx aluminium alloys at a slow speed as-quenched
Close research report.
Invention content
It is an object of the invention to overcome the deficiency of the prior art, it is big to provide a kind of improvement simple for process, easy to operate
The method of 7 line aluminium alloy of size intensity non-uniformity as caused by quenching；Process using the present invention can significantly improve conjunction
Gold greatly promotes the quenching degree of alloy in the hardness at the slow position of quenching rate.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, is at solution hardening
Aluminium alloy thick plate after reason carries out the cold rolling pre-treatment of total deformation >=10%, then, carries out artificial aging processing.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, the aluminium alloy thick plate
It is the aluminium alloy cast ingot plank that solution treatment obtains after Homogenization Treatments, hot rolling.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, the aluminium alloy thick plate
Thickness >=30mm.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, solid solution treatment process ginseng
Number is：460 DEG C -475 DEG C of solid solubility temperature, soaking time：0.5h-2h, water hardening to room temperature.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, aluminium alloy thick plate solid solution
To transfer time≤0.5h of cold rolling predeformation after quenching, transfer time is preferably≤15 minutes, more preferably≤10 minute, then
Preferably≤2 minute.
The present invention is a kind of to improve the method for intensity non-uniformity after the quenching of large scale 7 line aluminium alloy, cold rolling predeformation it is total
Deflection is 10%-50%；Multi-pass cold-rolling deformation is carried out, pass deformation≤8%, pass deformation is preferably 3-7%, more
Preferably 4-6%.
The present invention is a kind of to improve the method for intensity non-uniformity after the quenching of large scale 7 line aluminium alloy, after cold rolling predeformation
For plank to transfer time≤1h of artificial aging, transfer time is preferably 0.1-30 minutes, more preferably 0.1-15 minutes, then excellent
It is selected as 0.1-10 minutes.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, artificial aging technique ginseng
Number is：115-125 DEG C of aging temp, aging time 20-30h.
A kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches of the present invention, the Al-Zn-Mg-Cu
Alloy forms by mass percentage including following components：
Zn：3.8-7.0；Mg：1.5-2.8；Cu：0-2.6；Fe：＜ 0.35；Cr：＜ 0.3；Si：＜ 0.3；Ti：＜ 0.2；
Zr：＜ 0.25；V：＜ 0.1；Al：Surplus.
The present invention is a kind of to improve the method for intensity non-uniformity after the quenching of large scale 7 line aluminium alloy, treated aluminium alloy
In the case of not significantly reduced compared with the aluminium alloy surface hardness without pre-treatment, centre hardness improves 30%, is greatly decreased
The nonhomogeneous hardness of alloy surface and center portion.
Inventors discovered through research that：For 7xxx alloys by introducing predeformation, generated in alloy matrix aluminum more
Dislocation, can significantly improve in the case that alloy satiety solid solubility deficiency forming core power, promoted alloy in quenching condition at a slow speed
The precipitation rate of lower hardening constituent is made up the decrease of precipitating reinforcing effect brought due to the reduction of supersaturated quenching vacancy, substantially carried
Aging strength of the high alloy under quenching condition at a slow speed reaches 30% to the raising of alloy rigidity under as-quenched at a slow speed, makes up
Predeformation influences alloy property the blank of research under quenching condition at a slow speed.And predeformation is hard to the position of rapid quenching state
Degree slightly reduces, this is similar with the result of study of forefathers.Therefore, by introducing pre- become after large scale 7xxx aluminum alloy quenchings
Shape under the stiffness conditions for not significantly reducing alloy surface, can greatly improve the hardness of alloy center portion, so as to greatly improve alloy
The intensity non-uniformity as caused by quenching, making the intensity of alloy, overall performance is promoted in the case where meeting service condition.
Compared with prior art, the beneficial effects of the invention are as follows：
(1) forefathers improve the quenching sensitive of aluminium alloy and are mainly adjusted by alloying element, and design new alloy to large quantities of
The ripe application of amount is a quite very long and complicated process.The application of the present invention is ripe commercialization at present
7xxx aluminium alloys only add one of processing process, with regard to alloy intensity non-uniformity as caused by quenching can be significantly reduced,
It is easy to operate, it is applied widely.2xxx, 6xxx aluminium alloy of ageing strengthening are equally applicable in principle.
(2) process equipment of quenching is not needed to change, still using the method for conventional quenching, only after quenching
Introduce predeformation.
(3) due to introducing predeformation, alloy is provided simultaneously with the resultant effect of dislocation strengthening and precipitation strength after timeliness,
So that alloy still can keep higher hardness at the slow position of quenching rate, quenching degree is greatly improved, it is quick for height quenching
The alloy of perception, through hardening performance boost 30%, material for low-quenching sensitive or even to completely eliminate its quenching sensitive
Property.
Description of the drawings
Attached drawing 1 introduces predeformation with not having predeformation end quenching hardness figure for 7050 aluminium alloys.
Attached drawing 2 introduces predeformation with not having predeformation end quenching hardness retention curve for 7050 aluminium alloys.
Specific embodiment
With reference to specific embodiment, the present invention is further explained.It should be understood that the embodiment is merely illustrative this
Invention rather than restriction protection scope of the present invention.In practical applications technical staff according to the improvement made of the present invention and
Adjustment, still falls within protection scope of the present invention.
Aluminium alloy selected by example is 7050 aluminium alloy of general commercial, and quenching sensitive is very high, each alloying element tool
Body content is：Zn：6.1；Mg：2.2；Cu：2.3；Mn：0.1；Fe：0.15；Cr：0.04；Si：0.12；Ti：0.06；Zr：0.10；
Al：Surplus (wt.%).The alloy is full and uniformization treated hot rolled plate, thickness 35mm.
This example embodies influence of the predeformation for alloy quenching sensibility with end quenching experiment, and example chooses two groups
Sample, first group is without any processing, directly by end quenching after alloy solid solution, carries out T6 peak value timeliness later.Second
After group sample solid solution end quenching, introduce cold rolling reduction and be 20% pre-treatment, then carry out same T6 peak values timeliness,
Then the hardness data of two groups of experiments is compared.
First group of experiment：
(1) preparation of samples：Using the method for mechanical processing, aluminum alloy plate materials are processed into 35mm × 35mm × 120mm sticks
Shape sample.
(2) solution treatment：Sample is placed in air circulating oven, solid solution system is 475 DEG C of heat preservation 1h.
(3) end quenching：Quenching shift time is less than 10 seconds, and hardening media is 25 DEG C of water, and end water spout is a diameter ofFlow is 150L/h, and flow cannot be splashed to bar side, and the end quenching time is 6min.
(4) ageing treatment：Sample after end quenching is subjected to artificial aging processing immediately, institution of prescription for 120 DEG C/
24h。
Second group of experiment：
(1) preparation of samples：Using the method for mechanical processing, aluminum alloy plate materials are processed into 35mm × 35mm × 120mm sticks
Shape sample.
(2) solution treatment：Sample is placed in air circulating oven, solid solution system is 475 DEG C of heat preservation 1h.
(3) end quenching：Quenching shift time is less than 10 seconds, and hardening media is 25 DEG C of water, and end water spout is a diameter ofFlow is 150L/h, and flow cannot be splashed to bar side, and the end quenching time is 6min.
(4) predeformation：Sample after end quenching is subjected to cold-rolling deformation, in order to which the length for ensureing rods and bars of aluminium alloy is not sent out
Changing, cold rolling direction be sample width direction, by 4 passes deformation by 35mm cold rollings be 28mm, cold rolling reduction
20%, average draught per pass 5%.
(5) ageing treatment：Sample after predeformation is subjected to artificial aging processing immediately, institution of prescription for 120 DEG C/for 24 hours.
Interpretation of result：
By the sample obtained by two groups of experiments, sample is cut from center portion using the method for wire cutting, measurement distance quenched end
Hardness at different location section, the hardness of each 5 positions of section gauge choose hardness of the average value as the section, and
Hardness is drawn with the change curve with a distance from quenched end different cross section and hardness with from quenched end different cross section distance change
Hardness retention curve.Wherein hardness retention is the hardness in the section and the ratio of sample quenched end hardness.
1 7050 alloy end quenching hardness of table
It is as shown in table 1 the processed conventionally end quenching hardness of 7050 alloys, we can be found that the water cooling T6 shapes of alloy
State can reach the hardness of 180HV, however as apart from quenched end distance it is more remote, quenching rate slows down, and the hardness of alloy gradually drops
As low as 100HV or so, fall has reached 44%, shows very high quenching sensitive.
2 7050 alloy of table introduces end quenching hardness after predeformation
As shown in table 2 to introduce hardness of the predeformation under same institution of prescription after 7050 aluminium alloy end quenchings.From
In table it can be seen that after introducing predeformation, water cooling end hardness is 176HV, and compared to the state of no deformation, hardness slightly reduces
4HV, this is likely due to predeformation and accelerates the precipitation of follow-up timeliness precipitated phase roughening is caused to result in performance slightly
Decline.However colling end at a slow speed hardness stabilization in 130HV or so, hardness number is improved compared to the state of no predeformation
30HV.So by introducing predeformation so that in the case that alloy surface hardness declines 2.2%, centre hardness is not compared to having
Predeformation state promotes 30.0%
Being introduced into predeformation from 7050 aluminium alloys of Fig. 1 can be apparent with we in no predeformation end quenching hardness figure
Find out, after introducing predeformation, greatly improve alloy timeliness hardness under quenching condition at a slow speed, realize and ensureing hardenability
Under the premise of, greatly improve alloy centre hardness.Fig. 2 show the hardness retention change curve under two kinds of different conditions, from
We can also have found in figure, and by introducing predeformation, the hardness retention of the quenched end at a slow speed of 7050 aluminium alloys is improved by 55%
To 74%, the promotion amplitude for hardenability is 34.5%.Therefore, by introducing predeformation, greatly reduce alloy surface with
Centre hardness is poor, effectively improves the inhomogeneities of intensity after the quenching of 7 line aluminium alloys.
Claims (9)
1. it is to solution hardening treated aluminium a kind of method for improving intensity non-uniformity after the quenching of large scale 7 line aluminium alloy
Alloy plate carries out the cold rolling pre-treatment of total deformation >=10%, then, carries out artificial aging processing.
2. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 1, special
Sign is：The aluminium alloy thick plate is the aluminium alloy cast ingot plank that solution treatment obtains after Homogenization Treatments, hot rolling.
3. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 2, special
Sign is：Aluminium alloy thick plate thickness >=the 30cm.
4. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 2, special
Sign is：Solid solution treatment process parameter is：460 DEG C -475 DEG C of solid solubility temperature, soaking time：0.5h-2h, water hardening to room
Temperature.
5. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 1, special
Sign is：To transfer time≤0.5h of cold rolling predeformation after aluminium alloy thick plate solution hardening.
6. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 5, special
Sign is：The total deformation of cold rolling predeformation is 10%-50%；Carry out multi-pass cold-rolling deformation, pass deformation≤8%.
7. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 6, special
Sign is：Plank after cold rolling predeformation to artificial aging transfer time≤1h.
8. a kind of method for improving intensity non-uniformity after 7 line aluminium alloy of large scale quenches according to claim 7, special
Sign is：Artificial aging technological parameter is：115-125 DEG C of aging temp, aging time 20-30h.
9. intensity non-uniformity after a kind of 7 line aluminium alloy of improvement large scale quenching according to claim 1-7 any one
Method, it is characterised in that：The Al-Zn-Mg-Cu alloy forms by mass percentage including following components：
Zn：3.8-7.0；Mg：1.5-2.8；Cu：0-2.6；Fe：＜ 0.35；Cr：＜ 0.3；Si：＜ 0.3；Ti：＜ 0.2；Zr：＜
0.25；V：＜ 0.1；Al：Surplus.
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109457151A (en) * | 2018-12-14 | 2019-03-12 | 烟台南山学院 | A kind of high-strength/tenacity aluminum alloy plate and preparation method thereof |
| CN109898000A (en) * | 2019-03-29 | 2019-06-18 | 郑州轻研合金科技有限公司 | A kind of super high strength heat resistant alloy and preparation method thereof |
| CN110923525A (en) * | 2019-12-30 | 2020-03-27 | 天津忠旺铝业有限公司 | Preparation process of high-performance 7-series aluminum alloy sheet |
| CN111020323A (en) * | 2019-12-31 | 2020-04-17 | 湖南恒佳新材料科技有限公司 | Rolling method of ultrahigh-strength aluminum alloy plate |
| CN111471945A (en) * | 2020-06-03 | 2020-07-31 | 中南大学 | Hot forming method for improving comprehensive performance and surface quality of aluminum alloy component |
| JP2020125524A (en) * | 2019-02-06 | 2020-08-20 | アイシン軽金属株式会社 | Method for producing aluminum alloy member |
| CN111945084A (en) * | 2020-08-01 | 2020-11-17 | 安徽家园铝业有限公司 | Heat treatment process of aluminum alloy section |
| CN112921255A (en) * | 2021-01-15 | 2021-06-08 | 烟台南山学院 | Method for reducing quenching residual stress of 7000 series aluminum alloy thick plate and aluminum alloy plate |
| CN113186434A (en) * | 2021-04-13 | 2021-07-30 | 上海交通大学 | Stress corrosion resistant aluminum alloy material for automobile and preparation method thereof |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102978544A (en) * | 2012-11-21 | 2013-03-20 | 中南大学 | Method for multilevel creep age forming of Al-Zn-Mg-Cu series aluminium alloy plate |
| CN103184396A (en) * | 2012-11-21 | 2013-07-03 | 中南大学 | Creep aging forming method for Al-Zn-Mg-Cu aluminium alloy plate |
| CN103509984A (en) * | 2013-09-28 | 2014-01-15 | 中南大学 | Ultrahigh strength aluminum lithium alloy and preparation method thereof |
| CN104404414A (en) * | 2014-12-09 | 2015-03-11 | 中南大学 | 7075 aluminum alloy plate creep age forming method |
| CN106435417A (en) * | 2016-10-27 | 2017-02-22 | 福州大学 | Multistage deformation aging method for improving overall performance of 7xxx series aluminium alloy |
-
2018
- 2018-01-25 CN CN201810071578.4A patent/CN108265246A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102978544A (en) * | 2012-11-21 | 2013-03-20 | 中南大学 | Method for multilevel creep age forming of Al-Zn-Mg-Cu series aluminium alloy plate |
| CN103184396A (en) * | 2012-11-21 | 2013-07-03 | 中南大学 | Creep aging forming method for Al-Zn-Mg-Cu aluminium alloy plate |
| CN103509984A (en) * | 2013-09-28 | 2014-01-15 | 中南大学 | Ultrahigh strength aluminum lithium alloy and preparation method thereof |
| CN104404414A (en) * | 2014-12-09 | 2015-03-11 | 中南大学 | 7075 aluminum alloy plate creep age forming method |
| CN106435417A (en) * | 2016-10-27 | 2017-02-22 | 福州大学 | Multistage deformation aging method for improving overall performance of 7xxx series aluminium alloy |
Non-Patent Citations (3)
| Title |
|---|
| 催忠圻: "《金属学与热处理》", 31 October 1994 * |
| 张宏伟: "《铝锻造生产技术问答》", 30 April 2013 * |
| 李海 等: "预变形及时效处理对7055铝合金组织和性能的影响", 《稀有金属材料与工程》 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109457151A (en) * | 2018-12-14 | 2019-03-12 | 烟台南山学院 | A kind of high-strength/tenacity aluminum alloy plate and preparation method thereof |
| JP7366553B2 (en) | 2019-02-06 | 2023-10-23 | アイシン軽金属株式会社 | Method for manufacturing aluminum alloy parts |
| JP2020125524A (en) * | 2019-02-06 | 2020-08-20 | アイシン軽金属株式会社 | Method for producing aluminum alloy member |
| CN109898000A (en) * | 2019-03-29 | 2019-06-18 | 郑州轻研合金科技有限公司 | A kind of super high strength heat resistant alloy and preparation method thereof |
| CN110923525A (en) * | 2019-12-30 | 2020-03-27 | 天津忠旺铝业有限公司 | Preparation process of high-performance 7-series aluminum alloy sheet |
| CN111020323A (en) * | 2019-12-31 | 2020-04-17 | 湖南恒佳新材料科技有限公司 | Rolling method of ultrahigh-strength aluminum alloy plate |
| CN111471945A (en) * | 2020-06-03 | 2020-07-31 | 中南大学 | Hot forming method for improving comprehensive performance and surface quality of aluminum alloy component |
| CN111471945B (en) * | 2020-06-03 | 2021-04-02 | 中南大学 | Hot forming method for improving comprehensive performance and surface quality of aluminum alloy component |
| CN111945084A (en) * | 2020-08-01 | 2020-11-17 | 安徽家园铝业有限公司 | Heat treatment process of aluminum alloy section |
| CN112921255A (en) * | 2021-01-15 | 2021-06-08 | 烟台南山学院 | Method for reducing quenching residual stress of 7000 series aluminum alloy thick plate and aluminum alloy plate |
| CN113186434A (en) * | 2021-04-13 | 2021-07-30 | 上海交通大学 | Stress corrosion resistant aluminum alloy material for automobile and preparation method thereof |
| CN113909327A (en) * | 2021-09-22 | 2022-01-11 | 中北大学 | Pre-deformation die, pre-deformation method and preparation method of cylindrical part with outer longitudinal ribs |
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