CN102206794B - Method for enhancing mechanical property of ageing-strengthening aluminum-copper-magnesium-silver alloy subjected to solution-treated cold deformation - Google Patents
Method for enhancing mechanical property of ageing-strengthening aluminum-copper-magnesium-silver alloy subjected to solution-treated cold deformation Download PDFInfo
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Abstract
The invention discloses a method for enhancing the mechanical property of ageing-strengthening aluminum-copper-magnesium-silver alloy subjected to solution-treated cold deformation, which comprises the steps of: heating the ageing-strengthening aluminum-copper-magnesium-silver alloy subjected to the solution-treated cold deformation to 195 to 205 DEG C, preserving the temperature for 5 to 30 minutes, and carrying out high-temperature manual aging; then, reducing the temperature to 165 to 185 DEG C at the cooling speed of 40 to 80 DEG C/min; and after preserving the temperature for 6 to 20 hours for conducting peak ageing, tapping off and air cooling. The aluminum-copper-magnesium-silver alloy comprises the following components in percentage by weight: 4.3% to 4.96% of Cu, 0.2% to 0.28% of Mn, 0.39% to 0.81% of Mg, 0.52% to 1.2% of Ag, 0.1% to 0.25% of Zr and the balance of Al. The technological method disclosed by the invention is simple and reasonable; the ageing-strengthening aluminum-copper-magnesium-silver alloy subjected to the cold deformation obtains more fine and uniform dispersed omega phases through a two-stage ageing heat treatment technology; the adverse effect of the cold deformation on the separating-out of the omega phases of strengthening phases in the alloy is reduced; thereby, the mechanical property of the alloy at room temperature and high temperature is enhanced; and the alloy is suitable for industrial application.
Description
Technical field
The present invention relates to a kind of method that improves ageing strengthening aluminium-copper-magnesium-silver alloy mechanical property after the solid solution cold deformation.Belong to metallic substance heat treatment technics field.
Background technology
In the Al-Cu-Mg alloy of high Cu/Mg ratio, adding Trace Ag can bring out alloy and separate out a kind of new ageing strengthening phase (Ω phase).Because strengthening phase has high age hardening ability and good thermostability, make alloy phase ratios such as 2024,2618 of this alloy and Al-Cu-Mg system to have excellent more room temperature and mechanical behavior under high temperature.
This is that the timeliness of alloy is novel reinforced phase Ω and θ ' competition precipitation process mutually.Research shows that higher aging temp helps separating out of Ω phase, but the predeformation before the timeliness helps separating out of θ ' phase.Usually; Sheet alloy can deform after solution hardening; Sheet material in the actual production after the solution hardening need carry out straightening deformation; But the high density dislocation that straightening deformation is introduced has suppressed separating out of main strengthening phase Ω, promotes separating out of θ ' phase, thereby can reduce alloy at room temperature and mechanical behavior under high temperature.Therefore; How reduce or eliminate that straightening deformation is separated out Ω mutually and the disadvantageous effect of sheet material mechanical property through a kind of suitable aging treatment process; Improving alloy at room temperature and mechanical behavior under high temperature, is the problem of the Al-Cu-Mg-Ag alloy development exploitation solution of needing badly.
The multistage aging that occurs is at present handled (T6I4 and T6I6), for single-stage aging is handled T6, can improve the intensity and the fracture toughness property of alloy.Typical T6I4 treatment process comprises two stages; At first the high temperature lack time effect is handled the back quench cooled; 25～65 ℃ of low temperature aging for some time then; Its technological principle is to utilize fs high temperature lack time effect to improve the nucleation rate in G.P. district, under follow-up lesser temps, takes place then to separate out for the second time, thereby increases substantially the dispersity of enhanced particles and the mechanical property of alloy.T6I6 thermal treatment is the sample after handling through T6I4 to be brought up under the comparatively high temps proceed timeliness, and the G.P. district that makes separate out early stage changes to transition phase, further improves mechanical property.This shows that T6I4 and T6I6 handle and do not comprise two competition controls of separating out mutually, and second stage low temperature aging required time is long in T6I4 and the T6I6 thermal treatment process, is generally for 2 weeks, its process object is primarily aimed at the alloy that does not pass through deformation process.
Summary of the invention
The objective of the invention is to overcome the deficiency of prior art and a kind of process method advantages of simple is provided, can effectively improves room temperature and mechanical behavior under high temperature after the cold deformation of ageing strengthening aluminium-copper-magnesium-silver alloy solid solution, reduce or eliminate the method for cold deformation aluminium-copper-magnesium-silver alloy mechanical property disadvantageous effect.
The present invention improves that the method for ageing strengthening aluminium-copper-magnesium-silver alloy mechanical property is to adopt following proposal to realize after the solid solution cold deformation:
To pass through solid solution cold deformation ageing strengthening aluminium-copper-magnesium-silver alloy and be heated to 195-205 ℃, insulation 5-30min carries out the high temperature artificial aging; Then, be cooled to 165-185 ℃ with the speed of cooling of 40～80 ℃/min, after being incubated 6-20 hour and carrying out the peak value timeliness, the air cooling of coming out of the stove.
Among the present invention, the weight percent of the component of said aluminium-copper-magnesium-silver alloy is: Cu 4.3-4.96%, and Mn 0.2-0.28%, Mg0.39-0.81%, Ag 0.52-1.2%, Zr 0.1-0.25%, surplus is Al.
Among the present invention, said cold deformation is cold roller and deformed or cold drawn distortion; The deflection of said cold deformation is: 2-6%.
Among the present invention, said solid solubility temperature is: 505-515 ℃.
The present invention adopts above-mentioned process method, shows that through experiment high temperature helps separating out of Ω phase, is unfavorable for separating out of θ ' phase.Compare with low-temperature single-stage peak value timeliness (165-185 ℃); After the sheet alloy of straightening deformation adopts high temperature single-stage peak value timeliness (200 ℃) to handle; Help separating out of Ω phase, improved quantity and the ratio of Ω in precipitated phase, and improve the hot strength of alloy thus.But since alloy at high temperature the precipitated phase dispersity separated out of timeliness is low, cause alloy at room temperature intensity low.Compare with traditional single-stage aging peak value, after the sheet alloy of straightening deformation was handled through two-stage time effect, the quantity of Ω phase and dispersity increased, and its room temperature and high temperature tensile properties all obviously improve, and unit elongation still remains on higher level.
Compare with low-temperature single-stage peak value timeliness, after alloy adopted two-stage time effect to handle, the high-temperature aging of the first step helped separating out of Ω phase, and suppresses separating out of θ ' phase.In the high-temperature aging stage, the dislocation that cold deformation is introduced in the alloy is replied, and has reduced dislocation desity, has reduced the nucleation site of low temperature aging stage θ ' phase in the second stage, thereby has further suppressed separating out of θ ' phase simultaneously.Therefore, after alloy was handled through two-stage time effect, the quantity of θ ' phase obviously reduced, and the quantity of Ω phase and density significantly improve, and its room temperature and hot strength also improve simultaneously.
Compare with high temperature single-stage peak value timeliness; Alloy adopts two-stage time effect to handle; Growing up of Ω low temperature aging stage in the second stage of separating out in the high-temperature aging stage is slack-off; The continuation of low temperature aging stage promotes separating out of Ω phase as the core of Ω phase and the Ag-Mg atomic group that the high-temperature aging stage forms is in the second stage.And because the critical forming core radius of separating out under the low temperature is little, the nucleation rate of precipitated phase and dispersity are all high.Therefore, the quantity of not only separating out the Ω phase in the alloy increases, and the dispersity of precipitated phase also increases substantially, and makes the tensile property of sheet alloy under room temperature and high temperature of straightening deformation all be improved.
In sum; Process method advantages of simple of the present invention; Through the two-stage time effect thermal treatment process, make the ageing strengthening aluminium-copper-magnesium-silver alloy after the solid solution cold deformation obtain more Ω phase, reduce the disadvantageous effect of cold deformation to mechanical property; Thereby improve the tensile property of alloy under room temperature and high temperature, be suitable for industrial applications.
Description of drawings
Accompanying drawing 1 is the hardness curve synoptic diagram of the alloy 1 of the embodiment of the invention 1 through two-stage time effect and single-stage aging;
Accompanying drawing 2 (a) is TEM photo and the corresponding diffraction pattern thereof of alloy 1 behind 200 ℃ of timeliness 20min of the embodiment of the invention 1, shows the tiny Ω phase of alloy distribution, is difficult to observe θ ' phase.
Accompanying drawing 2 (b) is TEM photo and the corresponding diffraction pattern thereof of alloy 1 behind 200 ℃ of timeliness 2h of the embodiment of the invention 1, shows that the main precipitated phase of alloy is the Ω phase, separates out θ ' phase amount seldom.
Accompanying drawing 2 (c) is TEM photo and the corresponding diffraction pattern thereof of alloy 1 behind 165 ℃ of timeliness 20h of the embodiment of the invention 1, shows the tiny Ω phase of alloy disperse distribution, θ ' phase amount showed increased.
Accompanying drawing 2 (d) be the alloy 1 of the embodiment of the invention 1 at 200 ℃ of timeliness 20min the TEM photo of 165 ℃ of timeliness 20h and corresponding diffraction pattern thereof thereupon, show in the alloy and separate out Ω phase showed increased that θ ' compares the obvious minimizing among Fig. 2 (c).
Can know from accompanying drawing 1: alloy 1 is after two-stage time effect is handled, and hardness value is higher than the single-stage aging peak hardness, and it is identical with low-temperature single-stage timeliness time to peak that two-stage time effect is handled time to peak.
Show alloy 1 behind 200 ℃ of timeliness 20min from accompanying drawing 2 (a), the tiny Ω phase that distributes in the alloy substrate is difficult to observe θ ' phase.
Show alloy 1 behind 200 ℃ of timeliness 2h from accompanying drawing 2 (b), main precipitated phase is the Ω phase in the alloy substrate, separates out θ ' phase amount seldom.
Show alloy 1 behind 165 ℃ of timeliness 20h from accompanying drawing 2 (c), the tiny Ω phase of disperse distribution in the alloy substrate, θ ' phase amount showed increased.
From accompanying drawing 2 (d) show alloy 1 200 ℃ of timeliness 20min thereupon 165 ℃ of timeliness 20h and after, separate out Ω phase showed increased in the alloy substrate, θ ' compares the obvious minimizing among Fig. 2 (c).
Contrast accompanying drawing 2 (b)-(d) can be known: alloy high-temp ageing treatment θ ' obviously reduces mutually, and Ω increases mutually; After the two-stage time effect processing, separate out Ω phase showed increased, θ ' phase amount reduces.
Embodiment
Embodiment 1;
Alloy 1 composition is: 4.94%Cu, and 0.43%Mg, 1.04%Ag, 0.3%Mn, 0.15%Zr, surplus is an aluminium.Carry out solution treatment and shrend at 515 ℃, again through 2% straightening deformation, then 200 ℃ of timeliness 20 minutes, thereupon 165 ℃ of timeliness of low temperature 20 hours.Mechanical performance index through under the room temperature after this processing is seen table 1: tensile strength is 508MPa, and ys is 475MPa, and unit elongation is 10.7%; 250 ℃ of tensile mechanical properties: tensile strength is 323MPa, and ys is 315MPa, and unit elongation is 11.4%; 300 ℃ of tensile mechanical properties: tensile strength is 217MPa, and ys is 213MPa, and unit elongation is 12.4%.Can find out that from table 1 room temperature of alloy twin-stage ageing treatment and high temperature tensile properties are apparently higher than 165 ℃ of alloys and 200 ℃ of single-stage aging peak values.
Table 1
Embodiment 2;
Alloy 2 compositions are: 4.30%Cu, and 0.33%Mg, 0.52%Ag, 0.26%Mn, 0.17%Zr, surplus is an aluminium.Carry out solution treatment at 510 ℃, shrend is through 2% straightening deformation, then 200 ℃ of timeliness 30 minutes, thereupon 165 ℃ of timeliness of low temperature 20 hours.Mechanical performance index through under the room temperature after this processing is seen table 2: tensile strength is 498MPa, and ys is 475MPa, and unit elongation is 8.8%; 250 ℃ of tensile mechanical properties: tensile strength is 307MPa, and ys is 300MPa, and unit elongation is 12.6%; 300 ℃ of tensile mechanical properties: tensile strength is 206MPa, and ys is 201MPa, and unit elongation is 13.7%.Can find out that from table 2 room temperature and high temperature tensile properties that alloy 2 two-stage time effects are handled obviously are superior to 165 ℃ of alloys and 200 ℃ of single-stage aging peak values.
Table 2
Embodiment 3;
Alloy 3 compositions are: 4.87%Cu, and 0.81%Mg, 1.2%Ag, 0.27%Mn, 0.14%Zr, surplus is an aluminium.Carry out solution treatment and shrend at 505 ℃, through 6% straightening deformation, then 205 ℃ of timeliness 5 minutes, thereupon 185 ℃ of timeliness of low temperature 6 hours.Mechanical performance index through under the room temperature after this processing is seen table 3: tensile strength is 559MPa, and ys is 545MPa, and unit elongation is 8.9%; 250 ℃ of tensile mechanical properties: tensile strength is 364MPa, and ys is 357MPa, and unit elongation is 9.6%; 300 ℃ of tensile mechanical properties: tensile strength is 217MPa, and ys is 213MPa, and unit elongation is 10.2%.Can find out that from table 3 room temperature and high temperature tensile properties that alloy 3 two-stage time effects are handled are higher than 185 ℃ of alloys and 200 ℃ of single-stage aging peak values.
Table 3
Claims (2)
1. improve the method for ageing strengthening aluminium-copper-magnesium-silver alloy mechanical property after the solid solution cold deformation, it is characterized in that: the ageing strengthening aluminium-copper-magnesium-silver alloy that will pass through solid solution and cold deformation is heated to 195-205 ℃, is incubated 5-30min, carries out the high temperature artificial aging; Then, be cooled to 165-185 ℃ with the speed of cooling of 40～80 ℃/min, after being incubated 6-20 hour and carrying out the peak value timeliness, the air cooling of coming out of the stove; The weight percent of said aluminium-copper-magnesium-silver alloy compositions is: Cu 4.3-4.96%, and Mn 0.2-0.28%, Mg 0.39-0.81%, Ag0.52-1.2%, Zr 0.1-0.25%, surplus is Al; Said cold deformation is cold roller and deformed or cold drawn distortion; The deflection of said cold deformation is: 2-6%.
2. the method for ageing strengthening aluminium-copper-magnesium-silver alloy mechanical property after the raising solid solution cold deformation according to claim 1, it is characterized in that: said solid solubility temperature is: 505-515 ℃.
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| CN107151767A (en) * | 2017-01-20 | 2017-09-12 | 中国科学院金属研究所 | A kind of synchronous Strengthening and Toughening processing technology of Al Cu Mg alloys |
| CN108754364A (en) * | 2018-09-04 | 2018-11-06 | 钦州学院 | A kind of method of Ω phases Precipitation in Al-Cu-Mg alloy |
| RU2707114C1 (en) * | 2019-04-29 | 2019-11-22 | Федеральное государственное автономное образовательное учреждение высшего образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") | METHOD FOR THERMOMECHANICAL PROCESSING OF SEMI-FINISHED PRODUCTS FROM HEAT-STRENGTHENED Al-Cu-Mg-Ag ALLOYS |
| CN114855039B (en) * | 2021-02-03 | 2023-06-23 | 中国石油化工股份有限公司 | Al-Cu-Mg-Ag alloy and preparation method and application thereof |
| CN114875285B (en) * | 2022-04-11 | 2023-10-03 | 临沂矿业集团菏泽煤电有限公司彭庄煤矿 | Heat treatment method for corrosion resistance treatment of key alloy parts of mining equipment |
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| CN1556236A (en) * | 2003-12-30 | 2004-12-22 | 上海交通大学 | Titanium alloyed aluminium copper magnesium silver series high strength heat resistant aluminium alloy |
| CN101082115A (en) * | 2007-05-25 | 2007-12-05 | 中南大学 | Treatment method for providing aluminum alloy with high thermal stability anti-fatigue microstructure |
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| CN1556236A (en) * | 2003-12-30 | 2004-12-22 | 上海交通大学 | Titanium alloyed aluminium copper magnesium silver series high strength heat resistant aluminium alloy |
| CN101082115A (en) * | 2007-05-25 | 2007-12-05 | 中南大学 | Treatment method for providing aluminum alloy with high thermal stability anti-fatigue microstructure |
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| 马飞跃等.Ag含量对Al-Cu-Mg-Ag合金高温力学性能及耐热性的影响.《稀有金属材料与工程》.2010,第39卷(第3期),第482-485页. * |
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