CN106399777A - Ultrahigh-strength aluminum alloy with high strength and high hardenability and preparation method of ultrahigh-strength aluminum alloy - Google Patents
Ultrahigh-strength aluminum alloy with high strength and high hardenability and preparation method of ultrahigh-strength aluminum alloy Download PDFInfo
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- CN106399777A CN106399777A CN201611039989.2A CN201611039989A CN106399777A CN 106399777 A CN106399777 A CN 106399777A CN 201611039989 A CN201611039989 A CN 201611039989A CN 106399777 A CN106399777 A CN 106399777A
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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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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Abstract
The invention discloses ultrahigh-strength aluminum alloy with high strength and high hardenability and a preparation method of the ultrahigh-strength aluminum alloy. The ultrahigh-strength aluminum alloy comprises the components in percentage by weight: 5.8-6.4wt% of Zn, 1.8-2.6wt% of Mg, 1.0-1.2wt% of Cu, 0.06-0.20wt% of Zr, less than or equal to 0.08wt% of Fe, less than or equal to 0.06wt% Si and the balance of Al and unavoidable impurities. Compared with aluminum alloy such as AA7075 and AA7085, the effective strengthening phase of the alloy is remarkably optimized through reasonably controlling the contents of Zn, Mg and Cu, a Zn/Mg value and a Cu/Mg value in the alloy, therefore, the alloy keeps the hardenability of the aluminum alloy AA7085, and meanwhile, the strength of the alloy is obviously higher than the aluminum alloy such as AA7085; and an interdendritic second phase of the alloy is enabled to be sufficiently decomposed through controlling a homogenization heat treatment process, so that the content of elements which can be strengthened in the alloy is increased.
Description
Technical field
The present invention relates to a kind of high intensity high-hardenability ultra-high-strength aluminum alloy and preparation method thereof, belong to non-ferrous metal technology
Field.
Background technology
Ultra-high-strength aluminum alloy has the advantages that density is low, intensity is high, hot-working character good, is widely used in Aero-Space neck
The important structure member in domain.With the development of aerospace industry, for solving the problems that structural member welding is brought with riveting,
Improve overall performance and the reliability of equipment, mitigate equipment weight further, to super thick section (more than 150mm) Al-Zn-Mg-
Cu line aluminium alloy forging and pre-tensioned thick plate propose urgent requirement, that is, require novel ultra-high-strength aluminum alloy material except having
There is higher intensity, also should have the combination property such as preferable quenching degree and good fatigue behaviour.
At present, the external aeronautical plate ultra-high-strength aluminum alloy trade mark has the aluminium alloys such as AA7075, AA7X50, AA 7085, its
Middle AA7085 aluminium alloy alloy relatively advanced at present, has the combination properties such as high-hardenability high tenacity, is applied successfully to
The important load part such as spar of Boeing 787 undercarriage support member and Air Passenger A380 aircraft.But, AA7085 aluminium alloy is strong
Degree is relatively low, thus also reduces the safety coefficient of aircraft.Its reason is：Mg constituent content in alloy is relatively low, mainly by force
Change phase MgZn2The negligible amounts being formed, thus the intensity of alloy is relatively low.
In order to improve the service life of aircraft, increase the safety coefficient of aircraft, need to develop combination property more excellent
Ultra-high-strength aluminum alloy and its corresponding preparation method so as to be provided simultaneously with high intensity high-hardenability, improve aircraft overall performance
With service reliability, reduce the manufacturing cost of aircraft.
Content of the invention
Instant invention overcomes shortcoming of the prior art, there is provided a kind of high intensity high-hardenability ultra-high-strength aluminum alloy and its
Preparation method, to solve current aviation super thick section ultra-high-strength aluminum alloy in terms of combination property, particularly high intensity height is quenched
The deficiency of permeability aspect.
In order to solve above-mentioned technical problem, the present invention is achieved by the following technical solutions：
A kind of high intensity high-hardenability ultra-high-strength aluminum alloy, the percentage by weight of its composition is：Zn：5.8～6.4wt%,
Mg：1.8～2.6wt%, Cu：1.0～1.2wt%, Zr：0.06～0.20wt%, Fe：≤ 0.08wt%, Si：≤
0.06wt%, remaining group is divided into Al and inevitable impurity.
Further, micro- one or more of Mn, Cr, Ti are also contained, wherein micro- single content≤
0.05wt%, total content≤0.15wt%.
Further, the percentage by weight for 3: 1～5: 1, Cu and Mg for the percentage by weight of Zn and Mg is 0.4: 1～0.9: 1.
A kind of preparation method of high intensity high-hardenability ultra-high-strength aluminum alloy, comprises the following steps：
(1) it is first according to proportioning and carries out dispensing, carry out melting at 720～780 DEG C；
(2) molten metal being completely melt is refined, during refining, metal temperature maintains 700 DEG C～740 DEG C of scope
Interior, sufficient standing should be carried out after refining, time of repose is not less than 25 minutes；
(3) start after sufficient standing to cast, fire door temperature maintains in the range of 680 DEG C～720 DEG C；
(4) three-level homogenization is carried out to alloy casting blank, the first stage is incubated 3～15h, second stage at 360～420 DEG C
It is incubated 15～35h at 420～450 DEG C, the phase III is incubated 15～35h at 450～480 DEG C；
(5) warm-rolling is carried out to the strand after homogenization, start rolling temperature is 250～320 DEG C, total deformation rate more than 90%, eventually
Roll temperature control more than 200 DEG C；
(6) at 460～480 DEG C, solid solution, solution time 1～4h, room temperature water quenching are carried out to the sheet material after warm-rolling；
(7) in 4h after quenching, sheet material is carried out with the pre-stretching of 1.5～3% deflections；
(8) Ageing Treatment is carried out immediately to the sheet material after pre-stretching.
Wherein, in step (8), Ageing Treatment using peak value aging thermal treating process is：100 DEG C～170 DEG C heat 10～
64 hours.
Wherein, in step (8), Ageing Treatment using overaging Technology for Heating Processing is：First order aging temp 100～130
DEG C, aging time is 4～20h, and second level aging temp is 150～180 DEG C, and aging time is 4～20h.
Compared with prior art, the invention has the beneficial effects as follows：
A kind of high intensity high-hardenability ultra-high-strength aluminum alloy of the present invention and preparation method thereof, rationally controls in alloy
Zn, Mg, Cu content, Zn/Mg value, Cu/Mg value, compare AA7075, the aluminium alloy such as AA7085, alloy efficient hardening phase obtains significantly
Optimize, therefore alloy keeps the quenching degree of AA7085 aluminium alloy, and the intensity of alloy is apparently higher than aluminium alloys such as AA7085 simultaneously；
By controlling homogenizing heat treatment, make between alloy branch crystal second mutually fully to decompose, improve alloy and can strengthen unit
Cellulose content；Make Al3Even dispersion separates out Zr in the tissue, plays and farthest hinders recrystallization during warm-rolling and solid solution
Effect, further increase the combination property of alloy.
Specific embodiment
Hereinafter the preferred embodiments of the present invention are illustrated it will be appreciated that preferred embodiment described herein is only used
In the description and interpretation present invention, it is not intended to limit the present invention.
Below with reference to embodiment, technical solution of the present invention is further described：
Table 1 gives novel ultra-high-strength aluminum alloy chemical composition proposed by the invention and percentage by weight embodiment.
Table 1：Novel ultra-high-strength aluminum alloy chemical composition and percentage by weight
Table 1
The step of the preparation technology of this alloy is：
(1) by chemical composition and the percentage by weight requirement dispensing of alloy；
(2) melted in smelting furnace, fusion temperature is 720～780 DEG C；
(3) molten metal being completely melt is refined, during refining, metal temperature maintains 700 DEG C～740 DEG C of scope
Interior；
(4) sufficient standing should be carried out after refining, time of repose is not less than 25 minutes；
(5) start after sufficient standing to cast, fire door temperature maintains in the range of 680 DEG C～720 DEG C, pours and cast out 240mm
× 80mm × 10mm side's ingot；
(4) three-level homogenization is carried out to alloy casting blank, the first stage is incubated 3～15h, second stage at 360～420 DEG C
It is incubated 15～35h at 420～450 DEG C, the phase III is incubated 15～35h at 450～480 DEG C；
(5) warm-rolling is carried out to the strand after homogenization, start rolling temperature is 250～320 DEG C, total deformation rate more than 90%, eventually
Roll temperature control more than 200 DEG C；
(6) at 460～480 DEG C, solid solution, solution time 1～4h, room temperature water quenching are carried out to the sheet material after warm-rolling；
(7) in 4h after quenching, sheet material is carried out with the pre-stretching of 1.5～3% deflections；
(8) Ageing Treatment is carried out immediately to the sheet material after pre-stretching, selection aging technique is one of the following：
1. peak value aging thermal treating process is：Heat 10～64 hours at 100 DEG C～170 DEG C；
2. overaging Technology for Heating Processing is：100～130 DEG C of first order aging temp, aging time is 4～20h, the second level
Aging temp is 150～180 DEG C, and aging time is 4～20h.
Table 2 is the plate property of different aging techniques.
Table 2
The aging state performance of alloy of the present invention and the alloys such as AA7150, AA7085 are contrasted, as shown in table 3.
The combination property contrast of each alloy of table 3
Table 3
In table 3：Subscript 1. data source in SAE AMS.
In table 3：2. data is subscript：
In table 3：2. data is carried out respectively after peak value timeliness after room temperature water-cooled and air hardening subscript by alloy, both tensions
Intensity difference and the ratio of room temperature water cold front value timeliness tensile strength.
As can be seen from Table 3, the quenching degree of alloy of the present invention, apparently higher than AA7050 aluminium alloy, is slightly superior to AA7085 aluminium
Alloy, and tensile strength is apparently higher than AA7085 aluminium alloy.
In sum, alloy of the present invention has higher intensity and quenching degree, excellent combination property, is suitable for manufacture aircraft big
Type part, is conducive to improving globality and the reliability of aircraft, obtains distinct economic.
Finally it should be noted that：These are only the preferred embodiments of the present invention, be not limited to the present invention, although
With reference to embodiment, the present invention is described in detail, for a person skilled in the art, it still can be to aforementioned
Technical scheme described in each embodiment is modified, or carries out equivalent to wherein some technical characteristics, but all
Within the spirit and principles in the present invention, any modification, equivalent substitution and improvement made etc., should be included in the protection of the present invention
Within the scope of.
Claims (6)
1. a kind of high intensity high-hardenability ultra-high-strength aluminum alloy is it is characterised in that the percentage by weight of its composition is：Zn：5.8～
6.4wt%, Mg：1.8～2.6wt%, Cu：1.0～1.2wt%, Zr：0.06～0.20wt%, Fe：≤ 0.08wt%, Si：≤
0.06wt%, remaining group is divided into Al and inevitable impurity.
2. according to claim 1 a kind of high intensity high-hardenability ultra-high-strength aluminum alloy it is characterised in that also containing micro unit
One or more of plain Mn, Cr, Ti, wherein micro- single content≤0.05wt%, total content≤0.15wt%.
3. according to claim 1 a kind of high intensity high-hardenability ultra-high-strength aluminum alloy it is characterised in that the weight of Zn and Mg
Percentage is the percentage by weight of 3: 1～5: 1, Cu and Mg is 0.4: 1～0.9: 1.
4. according to claim 1 a kind of preparation method of high intensity high-hardenability ultra-high-strength aluminum alloy it is characterised in that bag
Include following steps：
(1) it is first according to proportioning and carries out dispensing, carry out melting at 720～780 DEG C；
(2) molten metal being completely melt is refined, during refining, metal temperature maintains in the range of 700 DEG C～740 DEG C, essence
Sufficient standing should be carried out, time of repose is not less than 25 minutes after refining；
(3) start after sufficient standing to cast, fire door temperature maintains in the range of 680 DEG C～720 DEG C；
(4) three-level homogenization is carried out to alloy casting blank, the first stage is incubated 3～15h at 360～420 DEG C, second stage exists
It is incubated 15～35h, the phase III is incubated 15～35h at 450～480 DEG C at 420～450 DEG C；
(5) warm-rolling is carried out to the strand after homogenization, start rolling temperature is 250～320 DEG C, total deformation rate more than 90%, finish to gauge temperature
Degree controls more than 200 DEG C；
(6) at 460～480 DEG C, solid solution, solution time 1～4h, room temperature water quenching are carried out to the sheet material after warm-rolling；
(7) in 4h after quenching, sheet material is carried out with the pre-stretching of 1.5～3% deflections；
(8) Ageing Treatment is carried out immediately to the sheet material after pre-stretching.
5. according to claim 4 a kind of preparation method of high intensity high-hardenability ultra-high-strength aluminum alloy it is characterised in that step
Suddenly in (8), Ageing Treatment using peak value aging thermal treating process is：Heat 10～64 hours at 100 DEG C～170 DEG C.
6. according to claim 4 a kind of preparation method of high intensity high-hardenability ultra-high-strength aluminum alloy it is characterised in that step
Suddenly in (8), Ageing Treatment using overaging Technology for Heating Processing is：100～130 DEG C of first order aging temp, aging time be 4～
20h, second level aging temp is 150～180 DEG C, and aging time is 4～20h.
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Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107245616A (en) * | 2017-05-31 | 2017-10-13 | 佛山科学技术学院 | A kind of 600MPa grades of low-quenching sensitive ultra-high-strength aluminum alloy and preparation method thereof |
| CN107460380A (en) * | 2017-09-04 | 2017-12-12 | 佛山科学技术学院 | A kind of anticorodal and preparation method thereof |
| CN106967936B (en) * | 2017-05-15 | 2018-08-31 | 广西南南铝加工有限公司 | A kind of preparation method of airfreight ultra-wide aluminium alloy sheet |
| CN108796321A (en) * | 2018-06-11 | 2018-11-13 | 中车青岛四方机车车辆股份有限公司 | A kind of Al-Zn-Mg alloy squeeze wood and its ingot homogenization technique and application containing Zr |
| 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 |
| CN109457149A (en) * | 2018-12-05 | 2019-03-12 | 天津忠旺铝业有限公司 | A kind of processing method of 7 line aluminium alloy slab |
| CN110699576A (en) * | 2019-10-24 | 2020-01-17 | 广西南南铝加工有限公司 | Preparation process of high-strength aluminum alloy precision casting plate |
| CN111826561A (en) * | 2019-12-31 | 2020-10-27 | 广东和胜工业铝材股份有限公司 | Al-Zn-Mg-Cu alloy and preparation process thereof |
| CN111850363A (en) * | 2020-06-18 | 2020-10-30 | 天津忠旺铝业有限公司 | High-damage tolerance type aluminum alloy for aviation and preparation method thereof |
| CN113234974A (en) * | 2021-05-07 | 2021-08-10 | 北京工业大学 | Method for reducing thermoplastic deformation resistance of Er microalloyed 7000 series aluminum alloy |
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106967936B (en) * | 2017-05-15 | 2018-08-31 | 广西南南铝加工有限公司 | A kind of preparation method of airfreight ultra-wide aluminium alloy sheet |
| CN107245616A (en) * | 2017-05-31 | 2017-10-13 | 佛山科学技术学院 | A kind of 600MPa grades of low-quenching sensitive ultra-high-strength aluminum alloy and preparation method thereof |
| CN107460380B (en) * | 2017-09-04 | 2019-07-09 | 佛山科学技术学院 | A kind of anticorodal and preparation method thereof |
| CN107460380A (en) * | 2017-09-04 | 2017-12-12 | 佛山科学技术学院 | A kind of anticorodal and preparation method thereof |
| CN108796321A (en) * | 2018-06-11 | 2018-11-13 | 中车青岛四方机车车辆股份有限公司 | A kind of Al-Zn-Mg alloy squeeze wood and its ingot homogenization technique and application containing Zr |
| CN108796321B (en) * | 2018-06-11 | 2020-06-02 | 中车青岛四方机车车辆股份有限公司 | Zr-containing Al-Zn-Mg alloy extrusion material and ingot casting homogenization process and application thereof |
| CN109457149A (en) * | 2018-12-05 | 2019-03-12 | 天津忠旺铝业有限公司 | A kind of processing method of 7 line aluminium alloy slab |
| 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 |
| CN110699576A (en) * | 2019-10-24 | 2020-01-17 | 广西南南铝加工有限公司 | Preparation process of high-strength aluminum alloy precision casting plate |
| CN110699576B (en) * | 2019-10-24 | 2021-04-13 | 广西南南铝加工有限公司 | Preparation process of high-strength aluminum alloy precision casting plate |
| CN111826561A (en) * | 2019-12-31 | 2020-10-27 | 广东和胜工业铝材股份有限公司 | Al-Zn-Mg-Cu alloy and preparation process thereof |
| CN111850363A (en) * | 2020-06-18 | 2020-10-30 | 天津忠旺铝业有限公司 | High-damage tolerance type aluminum alloy for aviation and preparation method thereof |
| CN113234974A (en) * | 2021-05-07 | 2021-08-10 | 北京工业大学 | Method for reducing thermoplastic deformation resistance of Er microalloyed 7000 series aluminum alloy |
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Effective date of registration: 20230803 Address after: 230000 floor 1, building 2, phase I, e-commerce Park, Jinggang Road, Shushan Economic Development Zone, Hefei City, Anhui Province Patentee after: Dragon totem Technology (Hefei) Co.,Ltd. Address before: No.18, Jiangwan 1st Road, Zhangcha street, Chancheng District, Foshan City, Guangdong Province Patentee before: FOSHAN University Effective date of registration: 20230803 Address after: 628000 No. 1-2, building 19, Guangyuan wanguanchuan Shaanxi Gansu hardware electromechanical building materials City, Yuanjiaba Industrial Park, economic and Technological Development Zone, Guangyuan City, Sichuan Province Patentee after: Guangyuan Botong Aluminum Co.,Ltd. Address before: 230000 floor 1, building 2, phase I, e-commerce Park, Jinggang Road, Shushan Economic Development Zone, Hefei City, Anhui Province Patentee before: Dragon totem Technology (Hefei) Co.,Ltd. |