CN107287537A - A kind of method for improving ultra-high-strength aluminum alloy plasticity - Google Patents
A kind of method for improving ultra-high-strength aluminum alloy plasticity Download PDFInfo
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- CN107287537A CN107287537A CN201710640235.0A CN201710640235A CN107287537A CN 107287537 A CN107287537 A CN 107287537A CN 201710640235 A CN201710640235 A CN 201710640235A CN 107287537 A CN107287537 A CN 107287537A
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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Abstract
A kind of method for improving ultra-high-strength aluminum alloy performance, it is characterized in that it mainly includes：Pre-treatment and subsequent reinforced heat treatment.Wherein pre-treatment includes：The hot compression of first time；Ultra-high-strength aluminum alloy Jing Guo hot compression is heated to after 400 DEG C, insulation 2h, progress ECAP extrusion process in mould is placed into；The thermal deformation that reduction ratio is 50% is carried out after 400 DEG C, insulation 0.5h will be again heated to by the ECAP ultra-high-strength aluminum alloys handled；The ultra-high-strength aluminum alloy for again passing by thermal deformation is carried out to 250 ± 5 DEG C × 24 h, 300 ± 5 DEG C × 6 h and 400 ± 5 DEG C × 6 h pre- recovery annealing processing.Subsequent reinforced heat treatment includes：Solid solution, Ageing Treatment.The alloy handled using pre-treating method of the present invention, then by follow-up fixation rates.Method is simple, easy to operate, it is processed by the invention after alloy plasticity be significantly improved, while other properties of alloy are also maintained or improved.
Description
Technical field
Method, especially a kind of raising side of ultra-high-strength aluminum alloy plasticity are improved the present invention relates to a kind of metal material plasticity
Method, specifically a kind of comprehensive utilization hot compression, ECAP, pre- reply, solid solution, ageing technique are moulded to improve ultra-high-strength aluminum alloy
The method of property.
Background technology
Al-Zn-Mg-Cu（7000）Alloy be a class it is important have high intensity, low-density and good hot-working character
The advantages of have alloy material, be the preferred structural material of aerospace field.In recent years, China's Aero-Space, bullet train,
Under the fast-developing promotion of automobile, 7000 be the focus that ultra-high-strength aluminum alloy also becomes research.But the deficiency of the alloy
Place is that fragility is big, and plasticity is poor.
In order to meet the use requirement under different condition, the plasticity of alloy must be improved.The adjustment of alloy composition and
The adjustment of strengthening treatment process is the main method for improving alloy property.7000 be that ultra-high-strength aluminum alloy belongs to ageing strengthening conjunction
Gold, the performance of alloy has stronger dependence to solid solution, aging technique.Therefore it is several main sides of alloy with reference to raising 7000
Method improves the alloy fragility greatly, the shortcoming of plasticity difference, has important practical significance to the plasticity for improving ultra-high-strength aluminum alloy.
The content of the invention
The purpose of the present invention is to be directed to existing Al-Zn-Mg-Cu（7000）The problem of ultra-high-strength aluminum alloy plastics are poor, hair
A kind of bright method for improving ultra-high-strength aluminum alloy plasticity.
The technical scheme is that：
A kind of method for improving ultra-high-strength aluminum alloy plasticity, it is characterised in that its pre-treatment and post processing, described pre-treatment is
The first time hot compression that carries out successively, effectively the Equal-channel Angular Pressing of crystal grain thinning, second of hot compression and pre- it can reply
Processing, described post processing is heat-treated for subsequent reinforced.
The hot compression of described first time is carried out after ultra-high-strength aluminum alloy is heated into 400 ± 5 DEG C, 2 ± 0.5h of insulation
Deflection is not less than 50% compression.
Described Equal-channel Angular Pressing be the ultra-high-strength aluminum alloy Jing Guo first time hot compression is again heated to 400 ±
5 DEG C, it is incubated after 2 ± 0.5h and is put into progress Equal-channel Angular Pressing processing in mould.
Second described of hot compression be the ultra-high-strength aluminum alloy by Equal-channel Angular Pressing is again heated to 400 ±
5 DEG C, it is incubated after 0.5h and carries out the deformation process that reduction ratio is not less than 50%.
Described pre- reply processing is that the ultra-high-strength aluminum alloy by second of hot compression is carried out into 250 ± 5 DEG C × 24 h
, 300 ± 5 DEG C × 6 h and 400 ± 5 DEG C × 6 h the processing of pre- recovery annealing.
Described subsequent reinforced heat treatment is solution treatment+Ageing Treatment.
Described solution treatment refer to by pretreatment ultra-high-strength aluminum alloy carry out 450 ± 5 DEG C × 2h, 460 ± 5 DEG C
× 2h and 470 ± 5 DEG C × 2h strengthened solution；The Ageing Treatment refers to the ultra-high-strength aluminum alloy Jing Guo solution treatment
Carry out water quenching immediately at normal temperatures, water-quenched slag is 25 ± 5 DEG C, then carry out the h of 100 DEG C × 0h~48（Gradient is 6h）Or
120℃×0 h~48 h（Gradient is 6h）Ageing Treatment.
Ultra-high-strength aluminum alloy involved in the present invention refers to that the As-extruded 7000 by homogenize process is（Al-Zn-Mg-
Cu）Alloy, it is mainly by aluminium（Al）, zinc（Zn）, magnesium（Mg）, copper（Cu）, zirconium（Zr）, strontium（Sr）Composition, wherein aluminium（Al）Matter
It is 77.56 ~ 85.24%, zinc to measure percentage（Zn）Mass percent 9.7 ~ 14.31%, magnesium（Mg）Mass percent for 2.5 ~
4.1%, copper（Cu）Mass percent 2.33 ~ 3.64%, zirconium（Zr）Mass percent 0.184 ~ 0.286%, strontium（Sr）Quality
Percentage 0.042 ~ 0.098%, each component sum is 100%.
Beneficial effects of the present invention：
（1）The alloy handled through the inventive method, plasticity tries to gain raising 95% or so.
（2）The alloy handled through the inventive method, the other parts performance of alloy is maintained or improved.
（3）Ultra-high-strength aluminum alloy plasticity of the present invention improves method, and simple to operate, equipment requirement is low, possesses well
Application prospect.
（4）The present invention provides reference for the follow-up plasticity for improving ultra-high-strength aluminum alloy.
Brief description of the drawings
Fig. 1 is the stretching fracture pattern of alloy of the embodiment one without pre-treatment of the present invention.
Fig. 2 is the stretching fracture pattern of the alloy of embodiment one by pre-treatment of the present invention.
Fig. 3 is the stretching fracture pattern of alloy of the embodiment two without pre-treatment of the present invention.
Fig. 4 is the stretching fracture pattern of the alloy of embodiment two by pre-treatment of the present invention.
Embodiment
The present invention is further illustrated with reference to the accompanying drawings and examples.
Embodiment one.
As shown in Figure 2.
The As-extruded that mass fraction is Al -13.01Zn -3.16Mg -2.8Cu -0.204Zr -0.0757Sr will be surveyed
After ultra-high-strength aluminum alloy, cutting sampling, the hot compression of first time is carried out, ultra-high-strength aluminum alloy is heated to 400 ± 5 DEG C, insulation 2
The compression that deflection is 50% is carried out after ± 0.5h；Ultra-high-strength aluminum alloy is heated to 400 ± 5 DEG C afterwards, insulation 2 ±
Cavity plate passage angle is placed into after 0.5hΦ=Equal-channel Angular Pressing processing is carried out in 110 ° of mould（Also other phases can be used
Same or equivalent mould carries out Equal-channel Angular Pressing）To refine the aluminium alloy crystal grain after first time hot compression；Afterwards by superelevation
Strength aluminum alloy carries out the thermal deformation that reduction ratio is 50% after being heated to 400 ± 5 DEG C, 0.5 ± 0.5h of insulation；Then by the strong aluminium of superelevation
Alloy carries out 250 ± 5 DEG C × 24 h, 300 ± 5 DEG C × 6 h and 400 ± 5 DEG C × 6 h three pre- recovery annealing processing.
Then, at the Intensive intervention that the h of h+470 ± 5 DEG C of 450 ± 5 DEG C ' 2 h+460 ± 5 DEG C ' 2 ' 2 is carried out to the alloy after pre- reply
Reason, water quenching immediately after solid solution terminates, water temperature is 25 ± 5 DEG C.After Water Quenching, 120 DEG C × 48 h are carried out to alloy（Can also be
100℃×48 h）Ageing Treatment.Finally to its hardness, conductance, intensity is measured, and XRD is carried out to it, and EBSD is analyzed,
Carry out intercrystalline corrosion, Peeling Corrosion experiment, to obtain the performance indications of each side during its peak value timeliness, and with only carrying out hot pressing
Contracting-Intensive intervention and the contrast of the sample of Ageing Treatment.
Experimental result is as follows（Table 1）：
Test result indicates that, at hot compression-Equal-channel Angular Pressing-hot compression-pre- reply pre-treatment and follow-up reinforcing timeliness
Manage and the hardness of Al -13.01Zn -3.16Mg -2.8Cu -0.204Zr -0.0757Sr alloys is had little to no effect, it is conductive
Rate is declined slightly.Hot compression-Equal-channel Angular Pressing-hot compression-pre- alloy replied after pre-treatment compared to only carry out a hot compression-
Solid gas coupling handles its elongation percentage and substantially got a promotion, i.e. the plasticity of material is significantly improved.Its anti intercrystalline corrosion ability and anti-stripping
Fall corrosive nature also to increase, crystallite dimension is also refined.The stretching fracture shape of alloy by pre-treatment of the present invention
Looks are as shown in Fig. 2 Fig. 1 is the stretching fracture shape appearance figure handled without present invention process.
Embodiment two.
As shown in Figure 4.
The As-extruded that mass fraction is Al -10.78Zn -2.78Mg -2.59Cu -0.22Zr -0.047Sr will be surveyed
After ultra-high-strength aluminum alloy, cutting sampling, the hot compression of first time is carried out, ultra-high-strength aluminum alloy is heated to 400 ± 5 DEG C, insulation 2
The compression that deflection is 50% is carried out after ± 0.5h；Ultra-high-strength aluminum alloy is again heated to 400 ± 5 DEG C, insulation 2 afterwards
Cavity plate passage angle is placed into after ± 0.5hΦ=110°（Also equal channel angular can be carried out using other identical or equivalent mould
Extruding）Mould in carry out ECAP extrusion process；Pressed after ultra-high-strength aluminum alloy is heated into 400 DEG C, insulation 0.5h afterwards
Lower rate is 50% thermal deformation；Then ultra-high-strength aluminum alloy is subjected to 250 ± 5 DEG C × 24 h, 300 ± 5 DEG C × 6 h and 400
± 5 DEG C × 6 h three pre- recovery annealing processing.Then, 450 DEG C ' 2 h+460 DEG C ' 2 h+ are carried out to the alloy after pre- reply
470 DEG C ' 2 h strengthened solution, water quenching immediately after solid solution terminates, water temperature is 25 ± 5 DEG C.After Water Quenching, alloy is entered
The h of row 120 DEG C × 48 Ageing Treatment.Finally to its hardness, conductance, intensity is measured, and XRD, EBSD points are carried out to it
Analysis, carries out intercrystalline corrosion, Peeling Corrosion experiment, to obtain the performance indications of each side during its peak value timeliness, and with only carrying out heat
Compression-Intensive intervention and the contrast of the sample of Ageing Treatment.
Experimental result is as follows（Table 2）：
Test result indicates that, hot compression-ECAP- hot compressions-pre- reply pre-treatment is to Al -10.78Zn -2.78Mg -2.59Cu
The hardness of -0.22Zr -0.047Sr alloys is had little to no effect, and conductance is improved, before hot compression-ECAP- hot compressions-pre- reply
Alloy after processing is substantially got a promotion compared to the elongation percentage for only carrying out hot compression-solid gas coupling processing, i.e., material plasticity is obtained
It is obviously improved.Its crystallite dimension is refined, and anti intercrystalline corrosion ability also increases.By the conjunction of pre-treatment of the present invention
The stretching fracture pattern of gold is as shown in figure 4, Fig. 3 is the stretching fracture shape appearance figure handled without present invention process.
Embodiment three.
The difference of the present embodiment and embodiment one is that the amount of first time compression and second of compression is 55%,
Last Ageing Treatment uses 100 DEG C × 48 h, and measured result and embodiment one are similar, thus illustrate, the first second compression
Effect of the amount increase of deformation and second of compression to the present invention is effective, therefore 50% is optimal compression deflection, meanwhile,
Applicant is also tested the technique that compress variation is less than 50%, and experimental data shows, when first time compression and the
When the amount of second-compressed deformation is less than 50%, elongation percentage is decreased obviously, and is increased by a year-on-year basis no more than 20%, it is difficult to meet use requirement.
Example IV.
The present embodiment and the difference of embodiment one are that last Ageing Treatment uses 100 DEG C × 0 h, 100 DEG C × 6
H, 100 DEG C × 12 h, 100 DEG C × 18h, 100 DEG C × 24 h, 100 DEG C × 30 h, 100 DEG C × 36 h, 100 DEG C × 42 h, actual measurement
Effect is close with embodiment one, or using 100 DEG C × 48 h be optimal.
Embodiment five.
The difference of the present embodiment and example IV is that last Ageing Treatment uses 120 DEG C × 0 h, 120 DEG C × 6
H, 120 DEG C × 12 h, 120 DEG C × 18h, 120 DEG C × 24 h, 120 DEG C × 30 h, 120 DEG C × 36 h, 120 DEG C × 42 h, actual measurement
Effect is close with embodiment one, or using 120 DEG C × 48 h be optimal.
Embodiment six.
The difference of the present embodiment and embodiment two is that the amount of first time compression and second of compression is 55%,
Last Ageing Treatment uses 100 DEG C × 48 h, the influence and embodiment three of the change of compress variation to experimental result
Close, less, performance parameter is close with embodiment two for the influence of the change of aging temperature to experimental result.
Embodiment seven.
What the difference of the present embodiment and embodiment six was that last Ageing Treatment is respectively adopted is：100 DEG C × 0 h, 100
DEG C × 6 h, 100 DEG C × 12 h, 100 DEG C × 18h, 100 DEG C × 24 h, 100 DEG C × 30 h, 100 DEG C × 36 h, 100 DEG C × 42
H, measured result is close with embodiment two, wherein being still optimal using 100 DEG C × 48 h.
Embodiment eight.
What the difference of the present embodiment and embodiment seven was that last Ageing Treatment is respectively adopted is：120 DEG C × 0 h, 120
DEG C × 6 h, 120 DEG C × 12 h, 120 DEG C × 18h, 120 DEG C × 24 h, 120 DEG C × 30 h, 120 DEG C × 36 h, 120 DEG C × 42
H, measured result is close with embodiment two, wherein being still optimal using 120 DEG C × 48 h.
Embodiment nine.
Mass fraction will be surveyed for Al -9.7Zn -2.5Mg -2.33Cu -0.184Zr -0.042Sr As-extruded to surpass
High strength alumin ium alloy, is handled using with the identical technique of embodiment one, and actual measurement parameter is also close with embodiment one.
Embodiment ten.
The As-extruded that mass fraction is Al -14.31Zn -4.1Mg -3.64Cu -0.286Zr -0.098Sr will be surveyed
Ultra-high-strength aluminum alloy, is handled using with the identical technique of embodiment two, and actual measurement parameter is also close with embodiment two.
Part that the present invention does not relate to is same as the prior art or can be realized using prior art.
Claims (8)
1. a kind of method for improving ultra-high-strength aluminum alloy plasticity, it is characterised in that its pre-treatment and post processing, described pre-treatment
For carry out successively first time hot compression, effectively the Equal-channel Angular Pressing of crystal grain thinning, second of hot compression and pre- can return
Multiple processing, described post processing is heat-treated for subsequent reinforced.
2. the method according to claim 1 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that the heat of described first time
Compression is to be heated to ultra-high-strength aluminum alloy to carry out compression change of the deflection not less than 50% after 400 ± 5 DEG C, 2 ± 0.5h of insulation
Shape.
3. the method according to claim 1 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that described equal channel angular
Extruding is to be put into mould after the ultra-high-strength aluminum alloy Jing Guo first time hot compression is again heated into 400 ± 5 DEG C, 2 ± 0.5h of insulation
Equal-channel Angular Pressing processing is carried out in tool.
4. the method according to claim 1 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that second described of hot pressing
Contracting is to carry out reduction ratio after the ultra-high-strength aluminum alloy by Equal-channel Angular Pressing is again heated into 400 ± 5 DEG C, insulation 0.5h
Deformation process not less than 50%.
5. the method according to claim 1 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that described pre- reply processing
It is that the ultra-high-strength aluminum alloy by second of hot compression is subjected to 250 ± 5 DEG C × 24 h, 300 ± 5 DEG C × 6 h and 400 ± 5
DEG C × 6 h pre- recovery annealing processing.
6. the method according to claim 1 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that described subsequent reinforced heat
It is processed as solution treatment+Ageing Treatment.
7. the method according to claim 7 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that described solution treatment is
Refer to the reinforcing that 450 ± 5 DEG C × 2h, 460 ± 5 DEG C × 2h and 470 ± 5 DEG C × 2h are carried out to the ultra-high-strength aluminum alloy by pretreatment
Solution treatment；The Ageing Treatment refers to the ultra-high-strength aluminum alloy Jing Guo solution treatment carrying out water quenching, water immediately at normal temperatures
Temperature of quenching is 25 ± 5 DEG C, then carries out the h of 100 DEG C × 0h~48（Gradient is 6h）Or the h of 120 DEG C × 0 h ~ 48（Gradient is 6h）
Ageing Treatment.
8. the method according to claim 1 for improving ultra-high-strength aluminum alloy plasticity, it is characterized in that the strong aluminium of described superelevation is closed
Gold is that the As-extruded 7000 Jing Guo homogenize process is（Al-Zn-Mg-Cu）Alloy, it is mainly by aluminium（Al）, zinc（Zn）, magnesium
（Mg）, copper（Cu）, zirconium（Zr）, strontium（Sr）Composition, wherein aluminium（Al）Mass percent be 77.56 ~ 85.24%, zinc（Zn）Matter
Measure percentage 9.7 ~ 14.31%, magnesium（Mg）Mass percent be 2.5 ~ 4.1%, copper（Cu）Mass percent 2.33 ~ 3.64%,
Zirconium（Zr）Mass percent 0.184 ~ 0.286%, strontium（Sr）Mass percent 0.042 ~ 0.098%, each component sum is
100%。
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112996934A (en) * | 2018-10-25 | 2021-06-18 | 霍尼韦尔国际公司 | ECAE treatment for high strength and high hardness aluminum alloys |
-
2017
- 2017-07-31 CN CN201710640235.0A patent/CN107287537A/en active Pending
Non-Patent Citations (1)
| Title |
|---|
| 张景玉: "热变形(压缩、ECAP)-预回复对高强度铝合金Al-10.78Zn-2.78Mg-2.59Cu-0.22Zr-0.047Sr组织性能的影响", 《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112996934A (en) * | 2018-10-25 | 2021-06-18 | 霍尼韦尔国际公司 | ECAE treatment for high strength and high hardness aluminum alloys |
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