CN105714223A - Homogenization heat treatment method of Al-Zn-Mg-Cu-Zr aluminum alloy - Google Patents
Homogenization heat treatment method of Al-Zn-Mg-Cu-Zr aluminum alloy Download PDFInfo
- Publication number
- CN105714223A CN105714223A CN201610152790.4A CN201610152790A CN105714223A CN 105714223 A CN105714223 A CN 105714223A CN 201610152790 A CN201610152790 A CN 201610152790A CN 105714223 A CN105714223 A CN 105714223A
- Authority
- CN
- China
- Prior art keywords
- heat treatment
- temperature
- homogenization heat
- aluminium alloy
- heating
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Conductive Materials (AREA)
Abstract
The invention relates to a homogenization heat treatment method of Al-Zn-Mg-Cu-Zr aluminum alloy. The homogenization heat treatment method of the Al-Zn-Mg-Cu-Zr aluminum alloy is characterized in that a three-level homogenization heat treatment process for controlling a heating process is used for homogenization heat treatment, and the homogenization heat treatment method comprises the following steps: (1) carrying out low-temperature pre-precipitation, and carrying out a first-level homogenization heat treatment process for promoting precipitation of Al3Zr as a dispersed phase; (2) insulating, and carrying out a second-level homogenization heat treatment process for increasing the overburnt temperature of a structure; and (3) carrying out a long-term uniform insulating process, and carrying out a third-level homogenization heat treatment process for eliminating high-melting-point Al2CuMg. By the heat treatment process, the problem of insufficient soaking in large cast ingots of 7xxx series aluminum alloy can be solved well, a coarse phase does not dissolve in a microscopic structure, an S phase is fully re-dissolved, and meanwhile, uniform precipitation of Al3Zr as the dispersed phase can be regulated and controlled. More importantly, the homogenization heat treatment method is suitable for industrial production of large cast ingots, and has good operability; meanwhile, homogenization heat treatment time can be shortened; and energy consumption of heat treatment is reduced.
Description
Technical field
The homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy, is specifically related to a kind of three grades of homogenizing heat treatment methods of Al-Zn-Mg-Cu-Zr aluminium alloy controlling temperature-rise period.
Background technology
Al-Zn-Mg-Cu system ultra-high-strength aluminum alloy has the advantage such as high specific strength and hardness, good processing characteristics, good corrosion resistance and higher toughness, is widely used in aerospace field.In recent years, in order to reduce cost, aircraft industry often adopt integral structure component replace the assembly parts being made up of a large amount of forging parts or extrusion.This market that has been aluminium alloy thick plate applications expanding in aircraft industry, also has higher requirement to the production technology level of large-size aluminum alloy ingot simultaneously.Al-Zn-Mg-Cu aluminium alloy is high due to alloying level, and in process of setting, dendritic segregation is serious, and as cast condition crystal boundary exists nonequilibrium thick eutectic structure, intracrystalline and Grain Boundary Chemistry composition and tissue distribution is uneven.Alloy substrate remains more thick crystalline phase, the main alloying elements such as Zn, Mg, Cu can be consumed and cause that aging strength reduces.Thick phase hinders the deformation process of matrix simultaneously, easily occurs that stress is concentrated in thick phase, and On Crack Propagation process has acceleration.Therefore, homogenization is heat-treated to as heat treatment step required before alloy deformation.
Homogenization Treatments can eliminate non-equilibrium low melting point phase and dendritic segregation, makes alloying element be uniformly distributed in solid solution, reduces the content of thick phase in microscopic structure.Meanwhile, in alloy, the interpolation of Zr can make alloy precipitate out the metastable Al with matrix coherence in Homogenization Process3Zr phase.Al3Zr is on good terms effectively pin crystal boundary after alloy solid solution, stops the migration of Grain and sub-grain boundary, retains substructure and dislocation, crystal grain thinning, strengthening matrix that rolling deformation produces.Meanwhile, the Al of small and dispersed3Zr makes recrystallization mark reduce, and high-angle boundary number reduces, and reduces the vantage point of η phase forming core, reduces the quenching sensitive of alloy.Therefore, optimize homogenizing heat treatment with the thick phase of abundant back dissolving, take into account the uniform precipitation of regulation and control disperse phase simultaneously, significant for the microscopic structure and combination property improving alloy.
Generally, the homogenization heat treatment of Al-Zn-Mg-Cu aluminium alloy can be divided into single-stage, twin-stage and multistage uniform metallization processes etc..Traditional single-stage homogenizing heat treatment mostly is 470 DEG C of insulation 24-48h, and in the 7xxx line aluminium alloy microscopic structure containing Zr of this PROCESS FOR TREATMENT, non-equilibrium eutecticum phase back dissolving is insufficient, and disperse phase Al3It is comparatively thick that Zr precipitates out size.For this, carried out twin-stage or multistage uniform heat-transformation Study on processing method both at home and abroad successively.Patent (CN201210287347.X) has invented a kind of three grades of homogenization heat treatment methods suitable in 7xxx line aluminium alloy, (465-473) DEG C/23-25h+ (480-485) DEG C/11-13h+ (495-500) DEG C/15-25min, this uniform heating process does not consider the uniform precipitation of disperse phase, high temperature, short time isothermal holding simultaneously, not only being difficult to accurately control in industrialization actual production, microscopic structure is also susceptible to burning simultaneously.Patent (CN200710022272.1) proposes the high-pressure uniform heat-transformation processing method eliminating thick phase in a kind of 7xxx aluminium alloy.By the feature of aluminum alloy melting temperature under high pressure effect, adopt higher temperature to carry out homogenization heat treatment, but the method is not particularly suited for the existing weaponry and equipment production line of aluminum current processing enterprise.
Summary of the invention
The purpose of the present invention is aiming at the deficiency that above-mentioned prior art exists, one is provided can effectively to shorten homogenization time, reduce intergranular last phase content, control disperse phase uniformly to precipitate out, the homogenization heat treatment method of the Al-Zn-Mg-Cu-Zr aluminium alloy of the final combination property improving production efficiency and product simultaneously.
It is an object of the invention to be achieved through the following technical solutions.
The homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy, it is characterised in that its homogenization heat treatment adopts the three grades of homogenizing heat treatment controlling temperature-rise period；Including: (1) low temperature precipitates out in advance, promotes disperse phase Al3The first order homogenizing heat treatment process that Zr precipitates out；(2) insulation, improves the second level homogenizing heat treatment process of tissue burnt temperature；(3) homogenization insulating process time long, eliminates high-melting-point Al2The third level homogenizing heat treatment process of CuMg.
A kind of homogenization heat treatment method of the Al-Zn-Mg-Cu-Zr aluminium alloy of the present invention, it is characterized in that described first order homogenizing heat treatment process is from the room temperature heating rate with 5～100 DEG C/h by Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot, heating-up time 3-30h, being raised to temperature is 300～450 DEG C, is incubated 3～15h；Wherein preferred technical scheme is, preferred 20-100 DEG C/h of heating rate, heating-up time preferred 4-20h, it is preferable that be raised to temperature and be 350-420 DEG C, the preferred 5-10h of temperature retention time.
A kind of homogenization heat treatment method of the Al-Zn-Mg-Cu-Zr aluminium alloy of the present invention, it is characterized in that described second level homogenizing heat treatment process is again by the Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot heating rate with 1～30 DEG C/h, heating-up time 2-10h, being raised to temperature is 460～475 DEG C, isothermal treatment for short time 0.5～10h；Wherein preferred technical scheme is, preferred 2-15 DEG C/h of heating rate, and heating-up time preferred 5-15h is raised to temperature and is preferably 465-475 DEG C；Temperature retention time is preferably 3-8h.
The homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy of the present invention, it is characterised in that described third level homogenizing heat treatment process is again by the Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot heating rate with 1～30 DEG C/h, heating-up time 1-10h.Warming temperature to 475～490 DEG C, is incubated 12-60h；Wherein preferred technical scheme is, preferred 2-10 DEG C/h of heating rate, heating-up time preferred 5-10h, preferred 475-485 DEG C of warming temperature, the preferred 24-48h of temperature retention time.
Compared with prior art, three grades of homogenizing heat treatment of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy controlling heating rate that the present invention relates to have three below remarkable advantage:
(1) by controlling temperature-rise period, solve dispersion phase precipitation and the problem of thick phase back dissolving simultaneously, shorten homogenization time, improve the thermal efficiency.
(2) ingot casting crystalline phase can fully be solid-solution in matrix, thus eliminating thick relative Fatigue Properties of Aluminum Alloy, and the adverse effect of fracture toughness etc..
(3) consider big ingot casting be heated in industrial heat treatment furnace inequality problem, adopt and increase by two grades of isothermal treatment for short time processes to control the temperature-rise period in high-temperature heating process, it is to avoid the microscopic structure burning that in industrial furnace, size ingot-casting causes due to inequality of being heated when being directly rapidly heated to 475-485 DEG C from the first order 300～420 DEG C greatly.
The homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy of the present invention, it is adaptable to 7050 and all Al-Zn-Mg-Cu-Zr aluminium alloys of other 7xxx alloy containing Zr element.Its Technology for Heating Processing is by controlling temperature-rise period to improve homogenization temperature further, it is not only able to realize intergranular last phase at utmost back dissolving, can promote that disperse phase uniformly precipitates out simultaneously, contribute to suppressing recrystallization and grain growth in hot-working and heat treatment process, thus improving microscopic structure and the combination property of alloy.Can effectively solving the technological deficiency that in existing uniform heating process, disperse phase and thick phase cannot be taken into account, while alloy strength level improves, fracture toughness and the fatigue behaviour of alloy are also improved.What is more important, the inventive method is applicable to the industrialized production of big ingot casting, and has good operability, and soaking time reduces, and the thermal efficiency improves.
Accompanying drawing explanation
Fig. 1 is the process schematic representation of the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy of the present invention.
Fig. 2 is scanning electron microscope undertissue pattern after 450mm thickness ingot casting employing 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h of present invention process all heat-treatment quenchings different from adopting 470 DEG C/48h of twin-stage uniform heating process；Wherein, (a) is 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h；B () is 400 DEG C/10h+470 DEG C/48h.
Fig. 3 is the as-cast structure of 520mm thickness ingot casting and DSC heating curve when being warming up at a slow speed 470 DEG C of insulation 0h.
Fig. 4 is scanning electron microscope undertissue pattern after 520mm thickness ingot casting employing 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h of present invention process all heat-treatment quenchings different from adopting 470 DEG C/48h of twin-stage uniform heating process；Wherein, (a) is 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h；B () is 400 DEG C/10h+470 DEG C/48h.
Fig. 5 is scanning electron microscope undertissue pattern after 600mm thickness ingot casting employing 400 DEG C/10h+470 DEG C/3h+480 DEG C/36h of present invention process all heat-treatment quenchings different from adopting 470 DEG C/48h of twin-stage uniform heating process；Wherein, (a) is 400 DEG C/10h+470 DEG C/3h+480 DEG C/36h；B () is 400 DEG C/10h+470 DEG C/48h.
Fig. 6 is disperse phase Al after the different heating rate uniform heating process of employing3The precipitation distribution of Zr particle；Wherein, (a) is embodiment 4；B () is comparative example 2.
Detailed description of the invention
A kind of homogenization heat treatment method of Al-Zn-Mg-Cu-Zr aluminium alloy, concrete technology flow process is as it is shown in figure 1, its technique comprises the following steps:
(1) first order, low temperature precipitates out in advance, promotes disperse phase Al3Zr precipitates out: metallic surface temperature is raised to 300～450 DEG C from room temperature with the average heating rate (heating-up time 3-30h) of 5～100 DEG C/h, is incubated 3～15h；Wherein preferred technical scheme is, preferred 20-100 DEG C/h of heating rate (heating-up time preferred 4-20h), preferred 350-420 DEG C of heating-up temperature, the preferred 5-10h of temperature retention time；
(2) second level, isothermal treatment for short time, improve tissue burnt temperature: the metallic surface temperature of aluminium alloy cast ingot step (1) processed is raised to 460～475 DEG C with the average heating rate (heating-up time 2-10h) of 1～30 DEG C/h, isothermal treatment for short time 0.5～10h；Wherein preferred technical scheme is, preferred 2-15 DEG C/h of heating rate (heating-up time preferred 5-15h), preferred 465-475 DEG C of heating-up temperature；The preferred 3-8h of temperature retention time.
(3) third level, homogenization insulating process time long, eliminate high-melting-point Al2CuMg (S) phase: aluminium alloy cast ingot metallic surface temperature step (2) processed is raised to 475～490 DEG C with the average heating rate (heating-up time 1-10h) of 1～30 DEG C/h, and is incubated 12-60h；Wherein preferred technical scheme is, preferred 2-10 DEG C/h of heating rate (heating-up time preferred 5-10h), preferred 475-485 DEG C of heating-up temperature, the preferred 24-48h of temperature retention time.
(4) after completing step (3), ingot casting is cooled to room temperature.
Below in conjunction with the drawings and the specific embodiments and way of contrast, the present invention is further elaborated, but the present invention is not limited to following example.
Embodiment 1
Al alloy component is by percentage to the quality: < 0.06wt.%, Zr0.1wt.%, Fe≤0.08wt.%, Si≤0.03wt.%, surplus is Al for Zn6.24wt.%, Mg2.06wt.%, Cu2.09wt.%, Ti.Semi-continuous casting becomes 450mm think gauge ingot casting.
Alloy adopts three grades of homogenization heat treating regimes of the inventive method to carry out Homogenization Treatments, specifically comprises the processes of: it is raised to 400 DEG C of insulation 10h from room temperature with the average heating rate (heating-up time 6.8h) of 55 DEG C/h, then proceed to be raised to 470 DEG C of insulation 3h with the average heating rate (heating-up time 7h) of 10 DEG C/h, be then raised to 480 DEG C of insulations 12h, 18h, 21h and 24h with the average heating rate (heating-up time 4h) of 2.5 DEG C/h again.
Embodiment 2
Al alloy component is by percentage to the quality: < < 0.06wt.%, Zr0.1wt.%, Fe≤0.08wt.%, Si≤0.03wt.%, surplus is Al for 0.10wt.%, Ti for Zn6.42wt.%, Mg2.08wt.%, Cu2.13wt.%, Mn.Semi-continuous casting becomes 520mm think gauge ingot casting.
Alloy adopts three grades of homogenization heat treating regimes of the inventive method to carry out Homogenization Treatments, specifically comprises the processes of: it is raised to 400 DEG C of insulation 10h from room temperature with the average heating rate (heating-up time 6.8h) of 55 DEG C/h, then proceed to be raised to 470 DEG C of insulation 3h with the average heating rate (heating-up time 7h) of 10 DEG C/h, be then raised to 480 DEG C of insulations 12h, 24h and 48h with the average heating rate (heating-up time 4h) of 2.5 DEG C/h again.
Embodiment 3
Al alloy component is by percentage to the quality: < 0.06wt.%, Zr0.1wt.%, Fe≤0.08wt.%, Si≤0.03wt.%, surplus is Al for Zn6.39wt.%, Mg2.09wt.%, Cu2.17wt.%, Ti.Semi-continuous casting becomes 600mm think gauge ingot casting.
Alloy adopts three grades of homogenization heat treating regimes of the inventive method to carry out Homogenization Treatments, specifically comprises the processes of: it is raised to 400 DEG C of insulation 10h from room temperature with the average heating rate (heating-up time 6.8h) of 55 DEG C/h, then proceed to be raised to 470 DEG C of insulation 3h with the average heating rate (heating-up time 7h) of 10 DEG C/h, be then raised to 480 DEG C of insulations 24h, 36h and 48h with the average heating rate (heating-up time 4h) of 2.5 DEG C/h again.
Embodiment 4
Al alloy component is by percentage to the quality: < 0.03wt.%, Zr0.1wt.%, Fe≤0.06wt.%, Si≤0.03wt.%, surplus is Al for Zn6.25wt.%, Mg2.1wt.%, Cu2.15wt.%, Ti.It is cast into ingot casting.
Alloy adopts three grades of homogenization heat treating regimes of the inventive method to carry out Homogenization Treatments, specifically comprises the processes of: heat to 400 DEG C of insulation 10h from room temperature with the average heating rate (heating-up time 6.8h) of 55 DEG C/h, then proceed to heat with the average heating rate (heating-up time 7h) of 10 DEG C/h to 470 DEG C of insulation 3h, be then raised to 480 DEG C of insulation 24h with the average heating rate (heating-up time 4h) of 2.5 DEG C/h again.
Comparative example 1
(1) traditional two-step homogenization heat treating regime is adopted to carry out Homogenization Treatments the embodiment 1 of different-thickness specification, embodiment 2 and embodiment 3 alloy cast ingot, specifically comprises the processes of: heat to 400 DEG C of insulation 10h with the average heating rate (heating-up time 6.8h) of 55 DEG C/h from room temperature, then heat to 470 DEG C of insulation 48h with the average heating rate (heating-up time 7h) of 10 DEG C/h.
(2) the multistage uniform heat-transformation resolving system of higher temperature is adopted to carry out Homogenization Treatments the 2-in-1 gold of embodiment, specifically comprises the processes of: heat to 400 DEG C of insulation 10h from room temperature with the average heating rate (heating-up time 6.8h) of 55 DEG C/h, it is incubated 3h with 10 DEG C/h average heating rate (heating-up time 7h) heating to 470 DEG C, then heats to 490 insulation 12h with the average heating rate (heating-up time 8h) of 2.5 DEG C/h again.
Comparative example 2
The homogenization heat treating regime being rapidly heated is adopted to carry out heat treatment embodiment 4 alloy, specifically comprises the processes of: heat to 470 DEG C of insulation 3h with the average heating rate (heating-up time 8h) of 55 DEG C/h from room temperature, then heat to 480 insulation 24h with the average heating rate (heating-up time 4h) of 2.5 DEG C/h again.
Table 1 shows microscopic examination result under embodiment homogenizing heat treatment different from comparative example and the endothermic peak area of S-phase corresponding on DSC heating curve.It can be seen that, for 450mm thickness size ingot-casting, after present invention process 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h homogenization heat treatment, S-phase area fraction is 0.06%, the S-phase area fraction 0.23% of relative twin-stage uniform heating process is decreased obviously, and heat treatment used time relative contrast's example 1 of present invention process reduces 20h, is effectively increased the thermal efficiency.Extending temperature retention time under present invention process at high temperature 480 DEG C, the area fraction of S-phase is in the trend reduced, and after 480 DEG C of insulation 21h, the endothermic peak area of S-phase is close to zero, substantially exists without S-phase in tissue.Fig. 2 is that 450mm thickness size ingot-casting adopts scanning electron microscope undertissue pattern after the different equal heat-treatment quenching of 470 DEG C/48h of 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h of present invention process and twin-stage uniform heating process.It can be seen that substantially exist without S-phase in microscopic structure under present invention process, relatively twin-stage uniform heating process is obvious for the back dissolving effect of thick phase.
Fig. 3 is 520mm think gauge embodiment 2-in-1 gold as-cast structure and the DSC heating curve being warming up at a slow speed 470 DEG C of insulation 0h.It can be seen that under 10 DEG C/h heats up at a slow speed, when temperature reaches 470 DEG C, now the endothermic peak of low melting point eutectic phase disappears, and in microscopic structure, burnt temperature has been increased to 485 DEG C, low melting point MgZn in microscopic structure2Change to S-phase completely mutually.Therefore, after 470 DEG C of isothermal treatment for short time make big ingot casting be heated evenly, higher temperature 480 DEG C can be heated to and carry out long-time soaking, without there is burning.And when homogenization heat treatment temperature is increased to 490 DEG C, microscopic structure generation burning, as shown in table 1.Fig. 4 is scanning electron microscope undertissue pattern after 520mm size ingot-casting employing 400 DEG C/10h+470 DEG C/3h+480 DEG C/24h of present invention process all heat-treatment quenchings different from adopting 470 DEG C/48h of twin-stage uniform heating process.It can be seen that for 520mm thickness size ingot-casting, microscopic structure exists without S-phase substantially under present invention process.As can be seen from Table 1, the heat treatment used time of twin-stage uniform heating process is relatively reduced 20h by present invention process, and now the endothermic peak area of S-phase is close to zero, substantially exists without S-phase in tissue.
Fig. 5 is that 600mm think gauge embodiment 3 alloy adopts scanning electron microscope undertissue pattern after the different equal heat-treatment quenching of 470 DEG C/48h of 400 DEG C/10h+470 DEG C/3h+480 DEG C/36h of present invention process and twin-stage uniform heating process.Present invention process is obvious relative to twin-stage uniform heating process thick phase back dissolving effect.As can be seen from Table 1, present invention process reduces 18h compared with the heat treatment used time of twin-stage uniform heating process, and now the endothermic peak area of S-phase is close to zero, substantially without S-phase in microscopic structure.Therefore, present invention process can effectively be applied on the big size ingot-casting of 600mm thickness.
As known from Table 1, after embodiment 4 alloy homogenization heat treatment in microscopic structure without S-phase.Disperse phase Al in two kinds of samples under different temperature-rise periods in embodiment 4 and comparative example 43The existence of Zr particle, as shown in Fig. 6 (a) and 6 (b), it can be seen that all occur in that the Al of Dispersed precipitate after heat treatment in alloy3Zr particle, and Al in sample after three grades of homogenization heat treatments under heating up at a slow speed3Zr particle is distributed more crypto set, Al in the sample that two states processes3The average diameter of Zr particle respectively 22nm and 35nm, precipitates out number density respectively 3.5 × 107Individual/mm2With 1.3 × 107Individual/mm2, as shown in table 2.Precipitation number density is more, precipitates out the more tiny disperse phase of size and is conducive to suppressing recrystallization and the grain growth of hot procedure.
Result of the test shows, the present invention is by conservative control temperature-rise period, each stage homogenization holding temperature and temperature retention time, it is possible to Al in effective regulation and control 7xxx system alloy3The distribution of Zr disperse phase, make disperse phase in the tissue uniformly, the distribution of disperse, thick phase obtains abundant back dissolving simultaneously.
Below it is only the concrete exemplary applications of the present invention, protection scope of the present invention is not constituted any limitation.The technical scheme that all employing equivalents or equivalence are replaced and formed, all falls within rights protection scope of the present invention.
Table 1 embodiment homogenizing heat treatment undertissue different from comparative example analyzes result
Al under table 2 embodiment homogenizing heat treatment different from comparative example3Zr disperse phase analyzes result
| Technique is numbered | Heat treatment process parameter | Average diameter/nm | Number density/mm2 |
| Embodiment 4 | 400℃/10h+470℃/3h+480℃/24h | 22 | 3.5×107 |
| Comparative example 2 | 470℃/3h+480℃/24h | 35 | 1.3×107 |
Claims (7)
1. the homogenization heat treatment method of an Al-Zn-Mg-Cu-Zr aluminium alloy, it is characterised in that its homogenization heat treatment adopts the three grades of homogenizing heat treatment controlling temperature-rise period；Including: (1) low temperature precipitates out in advance, promotes disperse phase Al3The first order homogenizing heat treatment process that Zr precipitates out；(2) insulation, improves the second level homogenizing heat treatment process of tissue burnt temperature；(3) homogenization insulating process time long, eliminates high-melting-point Al2The third level homogenizing heat treatment process of CuMg.
2. the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy according to claim 1, it is characterized in that described first order homogenizing heat treatment process is from the room temperature heating rate with 5～100 DEG C/h by Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot, heating-up time 3-30h, being raised to temperature is 300～450 DEG C, is incubated 3～15h.
3. the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy according to claim 1, it is characterized in that described second level homogenizing heat treatment process is again by the Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot heating rate with 1～30 DEG C/h, heating-up time 2-10h, being raised to temperature is 460～475 DEG C, and temperature retention time is 0.5～10h.
4. the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy according to claim 1, it is characterized in that described third level homogenizing heat treatment process is again by the Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot heating rate with 1～30 DEG C/h, heating-up time 1-10h.Warming temperature to 475～490 DEG C, temperature retention time is 12-60h.
5. the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy according to claim 1, it is characterized in that described first order homogenizing heat treatment process is from the room temperature heating rate with 20-100 DEG C/h by Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot, heating-up time 4-20h, being raised to temperature and be 350-420 DEG C, temperature retention time is 5-10h.
6. the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy according to claim 1, it is characterized in that described second level homogenizing heat treatment process is again by the Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot heating rate with 2-15 DEG C/h, heating-up time 5-15h, being raised to temperature and be 465-475 DEG C, temperature retention time is 3-8h.
7. the homogenization heat treatment method of a kind of Al-Zn-Mg-Cu-Zr aluminium alloy according to claim 1, it is characterized in that described third level homogenizing heat treatment process is again by the Al-Zn-Mg-Cu-Zr aluminium alloy cast ingot heating rate with 2-10 DEG C/h, heating-up time 5-10h.Warming temperature to 475-485 DEG C, is incubated 24-48h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610152790.4A CN105714223B (en) | 2016-03-17 | 2016-03-17 | A kind of homogenization heat treatment method of Al Zn Mg Cu Zr aluminium alloys |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610152790.4A CN105714223B (en) | 2016-03-17 | 2016-03-17 | A kind of homogenization heat treatment method of Al Zn Mg Cu Zr aluminium alloys |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105714223A true CN105714223A (en) | 2016-06-29 |
| CN105714223B CN105714223B (en) | 2017-05-31 |
Family
ID=56157870
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610152790.4A Active CN105714223B (en) | 2016-03-17 | 2016-03-17 | A kind of homogenization heat treatment method of Al Zn Mg Cu Zr aluminium alloys |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN105714223B (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107354412A (en) * | 2017-08-09 | 2017-11-17 | 中车青岛四方机车车辆股份有限公司 | A kind of Al Zn Mg alloy twin-stage homogenization process containing Zr |
| CN110964993A (en) * | 2019-12-17 | 2020-04-07 | 中铝材料应用研究院有限公司 | Grading homogenization treatment process for high-copper-magnesium-ratio Al-Zn-Mg-Cu-Zr ultrahigh-strength aluminum alloy cast ingot |
| CN111850436A (en) * | 2020-07-29 | 2020-10-30 | 中南大学 | Heat treatment method for simultaneously improving strength of high-strength and high-toughness aluminum alloy matrix and strength of welded joint |
| NO20191003A1 (en) * | 2019-08-20 | 2021-02-22 | Norsk Hydro As | Equipment and process for homogenization of cast products |
| CN112981289A (en) * | 2021-04-21 | 2021-06-18 | 中国航发北京航空材料研究院 | Stress relief annealing and homogenizing annealing method for 7000 series aluminum alloy ingot |
| CN114774814A (en) * | 2022-03-18 | 2022-07-22 | 云南云铝泽鑫铝业有限公司 | 6-series aluminum-magnesium-silicon alloy bar homogenizing heat treatment process |
| CN115094355A (en) * | 2022-07-01 | 2022-09-23 | 南京工业大学 | Two-stage slow furnace temperature rise homogenization heat treatment process for Al-Zn-Mg-Cu aluminum alloy |
| CN116065108A (en) * | 2023-04-06 | 2023-05-05 | 有研工程技术研究院有限公司 | Homogenization heat treatment method for high Cu content ultra-high strength corrosion-resistant 7xxx series aluminum alloy |
| CN117107172A (en) * | 2023-10-24 | 2023-11-24 | 中铝材料应用研究院有限公司 | Method for homogenizing aluminum alloy |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102732761A (en) * | 2012-06-18 | 2012-10-17 | 中国航空工业集团公司北京航空材料研究院 | 7000 series aluminum alloy material and preparation method thereof |
| CN102796976A (en) * | 2012-08-22 | 2012-11-28 | 北京有色金属研究总院 | Staged homogenization heat treatment method for improving microstructure and performances of Zr-containing 7xxx aluminum alloy |
| CN103459630A (en) * | 2011-06-10 | 2013-12-18 | 株式会社神户制钢所 | Aluminum alloy having excellent high-temperature characteristics |
| CN104109825A (en) * | 2014-07-04 | 2014-10-22 | 佛山市三水凤铝铝业有限公司 | Two-stage homogenizing heat treatment method for ultrahigh strength aluminium alloy cast ingot |
| CN105401021A (en) * | 2015-10-29 | 2016-03-16 | 中国航空工业集团公司北京航空材料研究院 | Aluminum alloy extruded sectional material at grade of 700 MPa |
-
2016
- 2016-03-17 CN CN201610152790.4A patent/CN105714223B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103459630A (en) * | 2011-06-10 | 2013-12-18 | 株式会社神户制钢所 | Aluminum alloy having excellent high-temperature characteristics |
| CN102732761A (en) * | 2012-06-18 | 2012-10-17 | 中国航空工业集团公司北京航空材料研究院 | 7000 series aluminum alloy material and preparation method thereof |
| CN102796976A (en) * | 2012-08-22 | 2012-11-28 | 北京有色金属研究总院 | Staged homogenization heat treatment method for improving microstructure and performances of Zr-containing 7xxx aluminum alloy |
| CN104109825A (en) * | 2014-07-04 | 2014-10-22 | 佛山市三水凤铝铝业有限公司 | Two-stage homogenizing heat treatment method for ultrahigh strength aluminium alloy cast ingot |
| CN105401021A (en) * | 2015-10-29 | 2016-03-16 | 中国航空工业集团公司北京航空材料研究院 | Aluminum alloy extruded sectional material at grade of 700 MPa |
Non-Patent Citations (2)
| Title |
|---|
| 杜科选等: "《铝电解和铝合金铸造生产与安全》", 31 May 2012, 冶金工业出版社 * |
| 王祝堂等: "《铝合金厚板生产技术与应用手册》", 31 January 2015, 中南大学出版社 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107354412A (en) * | 2017-08-09 | 2017-11-17 | 中车青岛四方机车车辆股份有限公司 | A kind of Al Zn Mg alloy twin-stage homogenization process containing Zr |
| NO20191003A1 (en) * | 2019-08-20 | 2021-02-22 | Norsk Hydro As | Equipment and process for homogenization of cast products |
| WO2021032850A1 (en) * | 2019-08-20 | 2021-02-25 | Norsk Hydro Asa | Equipment and method for homogenization of cast products |
| CN110964993A (en) * | 2019-12-17 | 2020-04-07 | 中铝材料应用研究院有限公司 | Grading homogenization treatment process for high-copper-magnesium-ratio Al-Zn-Mg-Cu-Zr ultrahigh-strength aluminum alloy cast ingot |
| CN111850436A (en) * | 2020-07-29 | 2020-10-30 | 中南大学 | Heat treatment method for simultaneously improving strength of high-strength and high-toughness aluminum alloy matrix and strength of welded joint |
| CN112981289B (en) * | 2021-04-21 | 2021-08-03 | 中国航发北京航空材料研究院 | Stress relief annealing and homogenizing annealing method for 7000 series aluminum alloy ingot |
| CN112981289A (en) * | 2021-04-21 | 2021-06-18 | 中国航发北京航空材料研究院 | Stress relief annealing and homogenizing annealing method for 7000 series aluminum alloy ingot |
| CN114774814A (en) * | 2022-03-18 | 2022-07-22 | 云南云铝泽鑫铝业有限公司 | 6-series aluminum-magnesium-silicon alloy bar homogenizing heat treatment process |
| CN115094355A (en) * | 2022-07-01 | 2022-09-23 | 南京工业大学 | Two-stage slow furnace temperature rise homogenization heat treatment process for Al-Zn-Mg-Cu aluminum alloy |
| CN116065108A (en) * | 2023-04-06 | 2023-05-05 | 有研工程技术研究院有限公司 | Homogenization heat treatment method for high Cu content ultra-high strength corrosion-resistant 7xxx series aluminum alloy |
| CN116065108B (en) * | 2023-04-06 | 2023-08-15 | 有研工程技术研究院有限公司 | Homogenization heat treatment method for high Cu content ultra-high strength corrosion-resistant 7xxx series aluminum alloy |
| CN117107172A (en) * | 2023-10-24 | 2023-11-24 | 中铝材料应用研究院有限公司 | Method for homogenizing aluminum alloy |
| CN117107172B (en) * | 2023-10-24 | 2024-02-09 | 中铝材料应用研究院有限公司 | Method for homogenizing aluminum alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN105714223B (en) | 2017-05-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105714223A (en) | Homogenization heat treatment method of Al-Zn-Mg-Cu-Zr aluminum alloy | |
| CN104532154B (en) | High rigidity height polishing pre-hardening plastic mould steel and preparation technology thereof | |
| CN105088118B (en) | A kind of ultra-fine crystallization method of nickel-based high-temperature alloy sheet material | |
| CN105200359B (en) | Reduce the heat treatment method of injection 7000 line aluminium alloy product stress of shaping | |
| CN105951008B (en) | A kind of Technology for Heating Processing of high-strength corrosion-resistant erosion aluminium alloy | |
| CN106435418A (en) | Heat treatment technology for improving intercrystalline corrosion resisting performance and stress corrosion resisting performance of 7-series aluminum alloy | |
| CN103409710A (en) | Aging heat treatment method of Al-Zn-Mg-Cu aluminum alloy | |
| CN104962847A (en) | Heat treatment technique for enhancing uniformity and corrosion resistance of 7-series alloy thick plate | |
| CN106834986A (en) | A kind of aviation alloyed aluminium homogenizing heat treatment | |
| CN109487184B (en) | Regression forming synchronous process for high-strength aluminum alloy in artificial aging state | |
| CN109207888A (en) | A kind of efficient creep age forming method of Al-Zn-Mg-Cu aluminum alloy plate non-isothermal | |
| CN109825748A (en) | A method of improving Al-Cu-Mg line aluminium alloy corrosion among crystalline grains | |
| CN104335707B (en) | A kind of 7xxx line aluminium alloy heat treating method | |
| CN101818315A (en) | Technology for regression and re-ageing heat treatment for ultra-high-strength aluminum alloy | |
| CN108034909A (en) | A kind of preparation method of 2050 aluminium lithium alloy fine grain plate | |
| CN104451291A (en) | Homogenizing heat treatment process of Er and Zr composite microalloyed Al-Zn-Mg-Cu alloy | |
| CN102286714A (en) | Preparation method of copper-nickel-tin alloy | |
| CN106148865B (en) | A kind of ageing hot processing method of Al-Mg-Zn alloys | |
| CN117758173A (en) | Al-Zn-Mg-Cu alloy based on strain-induced precipitation and particle-induced nucleation and preparation method and application thereof | |
| CN110952053B (en) | Cogging process of nickel-based superalloy, alloy device and application of alloy device | |
| CN110541131B (en) | Al-Cu-Li alloy thermomechanical treatment process based on particle-excited nucleation | |
| CN109402538B (en) | Natural aging state high-strength aluminum alloy regression forming synchronous process | |
| CN105369022B (en) | A kind of method that 2Cr12NiMo1W1V forging carries out crystal grain refinement in process of production | |
| CN115198213B (en) | Composite thermomechanical treatment method for regulating and controlling conductivity and mechanical property of aluminum alloy | |
| CN110079753A (en) | A kind of forging method for eliminating TiAl alloy remnants lamella |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20190923 Address after: 102209 Research Institute of Aluminum Science and Technology, Southern District of Future Science and Technology City, North Qijia Town, Changping District, Beijing Patentee after: China Aluminum Material Applied Research Institute Co Ltd Address before: 102209, Beiqijia Town, Beijing, Changping District City, future technology zone Patentee before: CHINALCO INSTITUTE OF SCIENCE AND TECHNOLOGY CO., LTD. |