CN101994072A - Heat treatment method for improving obdurability of 7-series high strength aluminium alloy - Google Patents
Heat treatment method for improving obdurability of 7-series high strength aluminium alloy Download PDFInfo
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Abstract
The invention relates to a heat treatment method for improving the obdurability of a 7-series high strength aluminium alloy, comprising the following steps: firstly carrying out double-stage forced solution treatment on the hot-processing 7***-series high strength aluminium alloy, namely, performing primary solution treatment for 2-4 hours at the temperature of 420-450 DEG C, and performing secondary reinforced solution treatment for 2-4 hours at the temperature of 450-490 DEG C; then quenching and cooling to room temperature, wherein the quenching medium is room temperature water; prestretching within 1-4 hours after quenching, wherein the prestretching distortion is 1-3%; performing high-temperature short-time ageing treatment, wherein the aging temperature is 120-180 DEG C and the aging time is 60-180min; quenching and cooling to room temperature after high-temperature short-time aging treatment, wherein the quenching medium is room temperature water; and finally carrying out low-temperature long-time aging treatment, wherein the aging temperature is 60-120 DEG C, and the aging time is 18-48 hours. The heat treatment method for improving the obdurability of a 7-series high strength aluminium alloy of the invention further improves the fracture toughness property of alloys and broadens the applied range of the aluminium alloys on the basis of maintaining the superhigh alloy strength.
Description
Technical field
The present invention relates to a kind ofly to improve 7 * * * heat treating method of series high-strength aluminum alloy obdurability, belong to metallic substance heat treatment technics field.
Background technology
7 * * * series high-strength aluminum alloy in, along with the raising of main alloy element content such as Zn, Mg, intensity rises and fracture toughness property reduces, and has limited the range of application of such alloy.In order to give full play to the advantage of high strength alumin ium alloy, need on the basis that keeps the strong alloy strength of superelevation not reduce, further improve the fracture toughness property of alloy.
7 * * * series high-strength aluminum alloy is typical ageing strengthening type aluminium alloy, makes the precipitation precipitated phase of a large amount of reasonable distribution of formation in the alloy reach the purpose of highly malleablized by rational heat treatment.In the evolution of existing alloy, for guaranteeing or improve the intensity of alloy, the normal content of alloying element that improves is (as B96,7055, and conventional solution treatment is difficult to make the abundant Hui Rong of precipitated phase 7093,7034 high-strength deformation aluminium alloys),, in solvable phase not fully under the situation of solid solution, the over-all properties of alloy is produced adverse influence.Degree of super saturation was both relevant with alloying constituent behind the alloy solid solution, and was also relevant with the solid solution system, and therefore for the ageing strengthening effect, improving solid solution strength is similar with the effect that increases alloying element content.
Burning when if temperature surpasses the fusing point of low melting point eutectic phase in the alloy or solidus temperature, just takes place in material easily when carrying out solution treatment, cause material property to descend.And the low melting point eutectic in the material is general polyphase eutectic combination phase mutually, the solution heat mechanics of each phase is different with dynamic conditions when high temperature, each mutually can be not simultaneously whole Hui Rong, but there is certain molten order that returns, when low melting point eutectic a certain mutually fully after the solid solution in mutually, the eutectic temperature of residue eutectic phase will improve, even temperature met or exceeded initial low melting point eutectic phase fusing point and also the eutectic remelt can not take place this moment, and traditional single-stage solid solution system is difficult to make the abundant Hui Rong of precipitated phase in the alloy structure, thereby influences the performance of material.
For the precipitation strength type aluminium alloy of certain ingredients, the character of crystal boundary that causes in the ag(e)ing process and crystal boundary precipitated phase, size, distribution and pattern develop has material impact to the alloy obdurability.Wherein, intracrystalline precipitated phase feature is the principal element of control alloy strength.Intracrystalline precipitated phase size is little, density is high and difficultly cut by slip dislocation, then helps alloy and obtains high strength; Crystal boundary precipitated phase feature then is to influence alloy flexible key factor, and crystal boundary precipitated phase quantity is few, is the spherical discontinuously arranged toughness that helps improving alloy.Therefore how to control crystal boundary and the differentiation of intracrystalline precipitated phase feature in the ag(e)ing process, make it be optimum distribution, bringing into play crucial effects for improving the alloy obdurability.
For lack time effect state alloy, because that the supersaturation solute atoms is separated out is insufficient, the density of strengthening phase is low and size is little in the matrix, and crystal boundary precipitated phase volume fraction is also less, so the toughness of alloy better and intensity is lower.
For peak value timeliness state alloy, the supersaturation solute atoms is fully separated out, and raising of precipitated phase volume fraction and size are bigger, and the intensity of alloy is higher.But the also corresponding increase of the precipitated phase volume fraction of crystal boundary also is continuous distribution, so alloy strength height and toughness is lower.
The technology for regression and re-ageing heat treatment of developing in recent years is to be incubated very short time (several seconds to several minutes) by the alloy with the peak value aging state at comparatively high temps (200～260 ℃), make the dissolving of intracrystalline strengthening phase, the generation alligatoring of crystal boundary precipitated phase also is discontinuously arranged, and then carry out a minor peaks timeliness, make alloy can obtain high intensity and fracture toughness property preferably, but this technology regression time is very short, is difficult in the actual industrial and uses.And because this method need be carried out two minor peaks timeliness to alloy, the technology relative complex, energy consumption is bigger.
Summary of the invention
At high strength alumin ium alloy intensity height and the problem of poor toughness, providing a kind of improves 7 * * * heat treating method of series high-strength aluminum alloy obdurability, on the basis that keeps the strong alloy strength of superelevation not reduce, further improve the fracture toughness property of alloy, enlarge the range of application of aluminium alloy.
Purpose of the present invention is achieved through the following technical solutions:
Improve 7 * * * heat treating method of series high-strength aluminum alloy obdurability, may further comprise the steps:
1) at first to hot-work 7 * * * series high-strength aluminum alloy carries out two-stage forced solution treatment, promptly earlier carries out the one-level solution treatment 2～4 hours under 420 ℃～450 ℃ temperature, carries out the secondary reinforcement solution treatment 2～4 hours again under 450 ℃～490 ℃ temperature;
2) carry out quench treatment after the two-stage forced solid solution and be cooled to room temperature, quenchant is a room temperature water;
3) carry out preliminary draft after the quench treatment in 1～4h, the pre-tension deformation amount is 1%～3%;
4) and then carry out the high temperature, short time ageing treatment, aging temp is 120 ℃～180 ℃, and aging time is 60min～180min;
5) carry out quench treatment after the high temperature, short time ageing treatment and be cooled to room temperature, quenchant is a room temperature water;
Ageing treatment when 6) low temperature is long more at last, aging temp is 60 ℃～120 ℃, aging time is 18h～48h.
Further, above-mentioned improvement 7 * * * heat treating method of series high-strength aluminum alloy obdurability, wherein, step 2) in quench transfer time less than 10 seconds.
Further, above-mentioned improvement 7 * * * heat treating method of series high-strength aluminum alloy obdurability, wherein, the transfer time of quenching in the step 5) was less than 30 seconds.
Substantive distinguishing features and obvious improvement that technical solution of the present invention is outstanding are mainly reflected in:
The present invention adopts two-stage forced solid solution treatment process, do not take place under the prerequisite of obvious recrystallize or grain growth in assurance, make the abundant Hui Rong of precipitated phase in the alloy, improve the degree of supersaturation of solute atoms, guarantee evenly separating out of precipitated phase small and dispersed in the follow-up ageing treatment process.From the control aging treatment process, by carrying out the high temperature, short time timeliness earlier, promote the forming core in rich solute atoms cluster of intracrystalline and GP district, high-temperature aging technology is 120 ℃～180 ℃/60min～180min, the low temperature aging temperature is 60 ℃～120 ℃.The present invention further improves the fracture toughness property of alloy on the basis that keeps the strong alloy strength of superelevation not reduce, enlarged the range of application of such aluminium alloy.
Description of drawings
Below in conjunction with accompanying drawing technical solution of the present invention is described further:
Fig. 1 is the metallographic microstructure of alloy after the two-stage forced solution treatment of embodiment 3 alloys;
Fig. 2 is the metallographic microstructure of alloy after the Comparative Examples 1 alloy single-stage solution treatment;
Fig. 3 is the intracrystalline of embodiment 3 alloys and the transmission electron microscope photo of crystal boundary precipitated phase;
Fig. 4 is the intracrystalline of Comparative Examples 1 alloy and the transmission electron microscope photo of crystal boundary precipitated phase.
Embodiment
The present invention improves 7 * * * heat treating method of series high-strength aluminum alloy obdurability, to the hot-work high strength alumin ium alloy carry out two-stage forced solution treatment, preliminary draft processing, high temperature, short time ageing treatment successively, ageing treatment when low temperature is long, specifically may further comprise the steps:
1) at first to hot-work 7 * * * series high-strength aluminum alloy carries out two-stage forced solution treatment, promptly earlier carries out the one-level solution treatment 2～4 hours under 420 ℃～450 ℃ temperature, carries out the secondary reinforcement solution treatment 2～4 hours again under 450 ℃～490 ℃ temperature; Do not take place to adopt two-stage forced solid solution craft under the prerequisite of recrystallize or grain growth guaranteeing, to make the abundant Hui Rong of precipitated phase in the alloy, to improve the degree of supersaturation of solute atoms, to guarantee evenly separating out of precipitated phase small and dispersed in the follow-up ageing treatment process;
2) carry out quench treatment after the two-stage forced solid solution and be cooled to room temperature, quenchant is a room temperature water, and the transfer time of quenching was less than 10 seconds;
3) carry out preliminary draft after the quench treatment in 1～4h, the pre-tension deformation amount is 1%～3%;
4) and then carry out the high temperature, short time ageing treatment, aging temp is 120 ℃～180 ℃, and aging time is 60min～180min;
5) carry out quench treatment after the high temperature, short time ageing treatment and be cooled to room temperature, quenchant is a room temperature water, and the transfer time of quenching was less than 30 seconds;
Ageing treatment when 6) low temperature is long more at last, aging temp is 60 ℃～120 ℃, aging time is 18h～48h.
From the control aging treatment process, by carrying out the high temperature, short time timeliness earlier, promote the forming core in rich solute atoms cluster of intracrystalline and GP district, and make crystal boundary that a spot of precipitated phase be arranged, then carry out the ageing treatment of low temperature when long, make the intracrystalline precipitated phase continue forming core and grow up, nodularization takes place in the crystal boundary precipitated phase in the low temperature aging process, enlarge the spacing of particle of crystal boundary precipitated phase, on the basis that guarantees alloy strength, significantly improve the fracture toughness property of high strength alumin ium alloy.
Embodiment 1:
With 7150 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.45%, and Mg 2.30%, and Cu 2.10%, and Zr 0.10%, and Fe 0.05%, and Si 0.01%, the Al surplus.
Two-stage forced solution treatment: 7150 alloys are carried out two-stage forced solution treatment, carried out the one-level solution treatment 4 hours under 420 ℃ of temperature, under 450 ℃ of temperature, carried out the secondary reinforcement solution treatment 4 hours then.
Quench treatment is cooled to room temperature after the two-stage forced solid solution, and quenchant is a room temperature water, and transfer time＜10s quenches.
Two-stage forced solution hardening is handled the back and carry out preliminary draft in 4h, and the pre-tension deformation amount is eliminated quenching stress 1.5%, improves the dislocation desity in the alloy.
With the alloy after the preliminary draft at 160 ℃ of timeliness 150min, behind the rapid quenching at 80 ℃ of timeliness 48h.
Embodiment 2:
With 7150 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.45%, and Mg 2.30%, and Cu 2.10%, and Zr 0.10%, and Fe 0.05%, and Si 0.01%, the Al surplus.
Two-stage forced solution treatment: 7150 alloys are carried out two-stage forced solution treatment, carried out the one-level solution treatment 3 hours under 435 ℃ of temperature, under 470 ℃ of temperature, carried out the secondary reinforcement solution treatment 2.5 hours then.
Quench treatment is cooled to room temperature after the two-stage forced solid solution, and quenchant is a room temperature water, and transfer time＜10s quenches.
Two-stage forced solution hardening is handled the back and carry out preliminary draft in 3h, and the pre-tension deformation amount is eliminated quenching stress 2.0%, improves the dislocation desity in the alloy.
With the alloy after the preliminary draft at 170 ℃ of timeliness 90min, behind the rapid quenching at 60 ℃ of timeliness 32h.
Embodiment 3:
With 7150 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.45%, and Mg 2.30%, and Cu 2.10%, and Zr 0.10%, and Fe 0.05%, and Si 0.01%, the Al surplus.
Two-stage forced solution treatment: 7150 alloys are carried out two-stage forced solution treatment, carried out the one-level solution treatment 2 hours under 450 ℃ of temperature, under 485 ℃ of temperature, carried out the secondary reinforcement solution treatment 2 hours then.
Quench treatment is cooled to room temperature after the two-stage forced solid solution, and quenchant is a room temperature water, and transfer time＜10s quenches.
Two-stage forced solution hardening is handled the back and carry out preliminary draft in 1h, and the pre-tension deformation amount is eliminated quenching stress 2.8%, improves the dislocation desity in the alloy.
With the alloy after the preliminary draft at 180 ℃ of timeliness 60min, behind the rapid quenching at 120 ℃ of timeliness 24h.
Embodiment 4:
With 7050 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.20%, and Mg 2.30%, and Cu 2.20%, and Zr 0.12%, and Fe 0.10%, and Si 0.05%, the Al surplus.
Two-stage forced solution treatment: 7050 alloys are carried out two-stage forced solution treatment, carried out the one-level solution treatment 3 hours under 435 ℃ of temperature, under 470 ℃ of temperature, carried out the secondary reinforcement solution treatment 2.5 hours then.
Quench treatment is cooled to room temperature after the two-stage forced solid solution, and quenchant is a room temperature water, and transfer time＜10s quenches.
Two-stage forced solution hardening is handled the back and carry out preliminary draft in 2h, and the pre-tension deformation amount is eliminated quenching stress 2.0%, improves the dislocation desity in the alloy.
With the alloy after the preliminary draft at 180 ℃ of timeliness 60min, behind the rapid quenching at 120 ℃ of timeliness 18h.
Embodiment 5:
With 7050 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.20%, and Mg 2.30%, and Cu 2.20%, and Zr 0.12%, and Fe 0.10%, and Si 0.05%, the Al surplus.
Two-stage forced solution treatment: 7050 alloys are carried out two-stage forced solution treatment, carried out the one-level solution treatment 2 hours under 450 ℃ of temperature, under 490 ℃ of temperature, carried out the secondary reinforcement solution treatment 2 hours then.
Quench treatment is cooled to room temperature after the two-stage forced solid solution, and quenchant is a room temperature water, and transfer time＜10s quenches.
Two-stage forced solution hardening is handled the back and carry out preliminary draft in 1h, and the pre-tension deformation amount is eliminated quenching stress 3.0%, improves the dislocation desity in the alloy.
With the alloy after the preliminary draft at 120 ℃ of timeliness 180min, behind the rapid quenching at 120 ℃ of timeliness 24h.
Comparative Examples 1
With 7150 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.45%, and Mg 2.30%, and Cu 2.10%, and Zr 0.10%, and Fe 0.05%, and Si 0.01%, the Al surplus.
7150 alloys are carried out carry out preliminary draft 2.5% in the 1h after the solution treatment of 475 ℃/4h, carry out then the thermal treatment of T6 peak value timeliness (120 ℃/24h).
Comparative Examples 2
With 7050 aluminum alloy plate materials behind the 25mm of 80% hot rolling deformation amount is example, and its chemical ingredients (massfraction %) is Zn 6.20%, and Mg 2.30%, and Cu 2.20%, and Zr 0.12%, and Fe 0.10%, and Si 0.05%, the Al surplus.
7050 alloys are carried out carry out preliminary draft 2.5% in the 1h after the solution treatment of 475 ℃/4h, carry out then the thermal treatment of T6 peak value timeliness (120 ℃/24h).
The mechanical property of 7150,7050 alloys sees Table 1 in the foregoing description and the Comparative Examples.
Table 1
| ? | Rm(Mpa)? | Rp0.2(Mpa)? | A(％)? | K IC |
| Embodiment 1 | 605? | 575? | 15.0? | 22.98? |
| Embodiment 2 | 615? | 595? | 14.0? | 23.31? |
| Embodiment 3 | 630? | 605? | 14.0? | 23.56? |
| Embodiment 4 | 602? | 580? | 14.8? | 22.89? |
| Embodiment 5 | 608? | 586? | 14.5? | 22.95? |
| Comparative Examples 1 | 588? | 515? | 17.2? | 20.68? |
| Comparative Examples 2 | 576? | 505? | 18.3? | 20.45? |
By table 1 as seen, adopt thermal treatment process of the present invention, when having improved alloy strength, fracture toughness property has had tangible improvement.
Shown by Fig. 1, Fig. 2, adopt two-stage forced solid solution of the present invention, the sufficient Hui Rong of the precipitated phase in the alloy structure has increased the degree of supersaturation of solute atoms, has improved the potentiality that material property promotes after the timeliness.
Shown by Fig. 3, Fig. 4, adopt aging technique of the present invention, crystal boundary precipitated phase size is big and be discontinuously arranged state, has improved the fracture toughness property of alloy material.
What need understand is: the above only is a preferred implementation of the present invention; for those skilled in the art; under the prerequisite that does not break away from the principle of the invention, can also make some improvements and modifications, these improvements and modifications also should be considered as protection scope of the present invention.
Claims (3)
1. improve the heat treating method of 7 series high-strength aluminum alloy obdurabilities, it is characterized in that may further comprise the steps:
1) at first hot-work 7 series high-strength aluminum alloys is carried out two-stage forced solution treatment, promptly earlier under 420 ℃～450 ℃ temperature, carried out the one-level solution treatment 2～4 hours, under 450 ℃～490 ℃ temperature, carried out the secondary reinforcement solution treatment 2～4 hours again;
2) carry out quench treatment after the two-stage forced solid solution and be cooled to room temperature, quenchant is a room temperature water;
3) carry out preliminary draft after the quench treatment in 1～4h, the pre-tension deformation amount is 1%～3%;
4) and then carry out the high temperature, short time ageing treatment, aging temp is 120 ℃～180 ℃, and aging time is 60min～180min;
5) carry out quench treatment after the high temperature, short time ageing treatment and be cooled to room temperature, quenchant is a room temperature water;
Ageing treatment when 6) low temperature is long more at last, aging temp is 60 ℃～120 ℃, aging time is 18h～48h.
2. the heat treating method of improvement 7 series high-strength aluminum alloy obdurabilities according to claim 1 is characterized in that: step 2) in quench transfer time less than 10 seconds.
3. the heat treating method of improvement 7 series high-strength aluminum alloy obdurabilities according to claim 1 is characterized in that: the transfer time of quenching in the step 5) was less than 30 seconds.
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| CN112410690A (en) * | 2020-11-20 | 2021-02-26 | 郭洋 | Aging treatment method for improving mechanical property of Al-Zn-Mg-Cu alloy |
| CN112410690B (en) * | 2020-11-20 | 2022-03-22 | 郭洋 | Aging treatment method for improving mechanical property of Al-Zn-Mg-Cu alloy |
| 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 |
| CN113106303A (en) * | 2021-03-31 | 2021-07-13 | 湖南大学 | Method for improving ZL114A alloy strength by combining Zn microalloying and double-stage aging system |
| CN113106303B (en) * | 2021-03-31 | 2021-12-14 | 湖南大学 | Method for improving ZL114A alloy strength by combining Zn microalloying and double-stage aging system |
| CN113528906A (en) * | 2021-06-21 | 2021-10-22 | 中车青岛四方机车车辆股份有限公司 | Wrought aluminum alloy and heat treatment method thereof |
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| CN113621903A (en) * | 2021-07-02 | 2021-11-09 | 江苏大学 | Heat treatment method for improving toughness of aluminum alloy |
| CN113621903B (en) * | 2021-07-02 | 2022-03-04 | 江苏大学 | Heat treatment method for improving toughness of aluminum alloy |
| CN115181921A (en) * | 2022-07-19 | 2022-10-14 | 佛山市深达美特种铝合金有限公司 | Heat treatment process for 7-series aluminum alloy extruded bar |
| CN117646155A (en) * | 2023-11-08 | 2024-03-05 | 东北轻合金有限责任公司 | Desolventizing phase control method for large-specification ultra-thick ultra-high-strength aluminum alloy plate |
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Application publication date: 20110330 |