CN104178670A - Ultrahigh strength aluminium alloy material and preparation method thereof - Google Patents
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Abstract
The invention relates to an ultrahigh strength aluminium alloy material and a preparation method thereof. The ultrahigh strength aluminium alloy material is characterized by comprising the following concrete components in percentage by weight: 12-14% of Zn, 2.4-3.2% of Mg, 1.0-1.5% of Cu, 0.2-0.5% of Zr, 0.1-0.3% of Mn, 0.1-0.6% of Ni and the balance of Al. The preparation method of the ultrahigh strength aluminium alloy material comprises the following steps: smelting raw materials, moulding a billet, carrying out machining deformation on the billet, carrying out solution treatment for 1 hour at the temperature of 450 DEG C and for 2 hours at the temperature of 475 DEG C, and carrying out manually intervened natural ageing treatment for 240-360 hours at the temperature of 70-80 DEG C. The ultrahigh strength aluminium alloy material is prepared by adopting a spray deposition technology, solution strengthening treatment is carried out on alloy, and aging treatment, carried out for 240-360 hours at the temperature of 70-80 DEG C, instead of the traditional natural ageing treatment is adopted, so that natural ageing time is shortened, and mechanical properties of the alloy are improved; meanwhile, the developed ultrahigh strength alloy is uniform and tiny in structure, has no macrosegregation and has the performances that tensile strength is 780-820MPa, yield strength is 700-740MPa, elongation percentage is 9-13% and fracture toughness property is 30-35MPa.m<1/2>, so that overall performance of the ultrahigh strength aluminum alloy material is at the international advanced level.
Description
Technical field
The invention belongs to aluminium alloy technical field, relate in particular to a kind of ultrahigh-strength aluminum alloy material that adopts spray deposition technology development and preparation method thereof.
Background technology
It is little that ultra-high-strength aluminum alloy has density, intensity is high, machine adds superior performance, specific tenacity is high, the advantages such as corrosion resistance nature is good, being widely used in aerospace industry and civilian technique, is one of primary structure material of current aerospace industry, is also used widely in communications and transportation and other industrial sector simultaneously.7000 line aluminium alloys are class high-strength/tenacity aluminum alloy materials of developing taking aircraft stock as background in the world the forties in 20th century and growing up, the 7000 line aluminium alloy materials that tradition is used are generally to obtain final various section bar products by operations such as ingot casting, cold and hot deformation processing, thermal treatments, the manufacture that is widely used in for a long time high-strength structure part etc. in various airframes, wingbar, cabin wallboard and rocket is indispensable important materials in the aerospace industry of countries in the world.At present 7000 line aluminium alloy products of the tens of kinds of different-alloy ingredient standard trades mark have been developed in the whole world, corresponding alloy thermal treatment standard technology more reach hundreds of more than.Along with the development of aerospace industry and civilian industry, scientific research personnel recognizes that the plasticity of high strength alumin ium alloy and fracture toughness property have become the further bottleneck of application of this alloy of restriction gradually.Past scientific research personnel pursues high strength simply and has ignored plasticity and fracture toughness property, along with the development of fracture mechanics, and the application of fail safety principle of design in real work, people to structured material particularly the understanding of the importance of high strength alumin ium alloy fracture toughness property and plasticity become clearer.At present and tensile strength, anticorrosive, fatigue resistance is listed as 4 main performance assessment criteria of aluminium alloy for plasticity and fracture toughness property index.
But plasticity index is often conflicting with intensity index, in plasticity and toughness raising, intensity tends to decline.For example, international and the domestic two-stage time effect process that generally adopts is put forward heavy alloyed plasticity and fracture toughness property at present, but adopt this technique to put forward heavy alloyed plasticity and fracture toughness property must to be accompanied by the reduction of strength of alloy and yield strength, therefore seek the technique that a kind of high strength and high-ductility toughness coexists is the direction that scientific research personnel makes great efforts always.
Current unique technique that can make intensity and plasticity toughness simultaneously improve is crystal grain thinning, therefore wants to put forward heavy alloyed plasticity and toughness and just must make the grain refining of this alloy.And the main technique that makes at present the grain refining of alloy is exactly fast solidification technology, spray deposition technology, as the Typical Representative of fast solidification technology, is widely used in recent years.In long-term scientific research, scientific research personnel finds the content by improving Zn element in 7000 line aluminium alloys, can effectively improve the over-all properties of alloy, but in the time that the content of Zn element in alloy exceedes 8%, because the crystallisation range of this class alloy is wide, between precipitated phase and matrix, difference of specific gravity is large, in the time adopting the aluminium alloy of traditional this class high Zn content of explained hereafter, easily cause the coarse grains in alloy, and there is obvious macrosegregation, inside ingot easily produces decrepitation, therefore adopt the Zn content of 7000 line aluminium alloys of traditional explained hereafter to be generally no more than 8%, also make the ultimate tensile strength of 7000 line aluminium alloys of traditional technology production be difficult to break through this high point of 700MPa simultaneously.
The appearance of spray deposition technique, make various countries' industry member break through traditional 8%Zn containing quantitative limitation, developing a new generation 7000 is that ultra-high-strength aluminum alloy comes true, while adopting spray deposition technique preparation to exceed 8% aluminium alloy containing Zn amount, because the crystal grain in alloy is by significantly refinement, various both macro and micro segregations are suppressed, can effectively control the inner tendency that produces hot tearing in deposition blank process of setting, simultaneously because setting rate is accelerated, the degree of supersaturation of various alloying elements in blank is increased, in follow-up heat treatment process various precipitated phases separate out more abundant, be conducive to material and obtain more superior mechanical property.
The domestic research unit that is engaged in jet deposition superalloyization 7000 line aluminium alloys mainly contains the units such as Beijing Non-Fervoous Metal Inst., University of Science & Technology, Beijing, BJ University of Aeronautics & Astronautics.If the composition of jet deposition 7000 line aluminium alloys of Beijing University of Science & Technology's research is Al-8.8%Zn-3.0%Mg-1.7%Cu-1.0%Mn-0.12%Zr, adopt peak aging technique; The composition of jet deposition 7000 line aluminium alloys of Central South University is Al-8.3%Zn-2.04%Mg-2.3%Cu-0.16%Zr, adopts the i.e. 120 DEG C of 24h of peak aging technique, its tensile strength, and yield strength and unit elongation reach respectively 648MPa, 630MPa and 11.2%; It is Al-11.3%Zn-2.4%Mg-1.0%Cu-0.3%Zr-0.5%Ni that Inner Mongol University of Technology adopts the composition of 7000 line aluminium alloys of spray deposition technology development, adopt the i.e. 130 DEG C of 24h of peak aging technique, tensile strength, yield strength and unit elongation are respectively 849MPa, 796MPa and 3.3%.The aging technique relating in disclosed report at present has peak timeliness, two-stage time effect and regression and re-ageing, and the technique that does not relate to natural aging is reported.
Summary of the invention
First technical problem to be solved by this invention is to provide a kind of ultrahigh-strength aluminum alloy material of high comprehensive performance.
Second technical problem to be solved by this invention is to provide that a kind of technique is simple, the preparation method of easy-operating ultrahigh-strength aluminum alloy material, adopt strengthened solution in conjunction with manual intervention natural aging treatment, the aluminium alloy making not only has high strength and high tenacity, has greatly reduced again natural aging time simultaneously.
The present invention solves the technical scheme that above-mentioned first technical problem adopts: a kind of ultrahigh-strength aluminum alloy material, is characterized in that: the mass percent of the concrete composition of this aluminum alloy materials is Zn:12%-14%; Mg:2.4%-3.2%; Cu:1.0%-1.5%; Zr:0.2%-0.5%; Mn:0.1%-0.3%; Ni:0.1%-0.6%; Surplus is Al.
The present invention solves the technical scheme that above-mentioned second technical problem adopt: a kind of preparation method of ultrahigh-strength aluminum alloy material, is characterized in that comprising the following steps:
1) per-cent that weighs is Zn:12%-14%; Mg:2.4%-3.2%; Cu:1.0%-1.5%; Zr:0.2%-0.5%; Mn:0.1%-0.3%; Ni:0.1%-0.6%; Surplus be the material of Al as the starting material of this alloy, wherein Cu adopts Al-50Cu master alloy, Ni adopts Al-20Ni master alloy, all the other are pure metal;
2) the above-mentioned alloy raw material Al weighing up, Al-50Cu master alloy, Al-Ni master alloy are put into medium-frequency induction furnace, energising adds until the metal in crucible dissolves, when being risen to 720 DEG C-740 DEG C, melt temperature adds Zr particle and pure Mn sheet, after fully stirring, melt temperature is risen to 800 DEG C-820 DEG C, after power-off, adopt graphite to press spoon to be pressed into pure Zn and pure Mg, fully stir, melt temperature is risen to 720 DEG C-750 DEG C;
3) adopt refining agent and alterant and C2Cl6 degasifier to go bad and refining treatment to melt;
4) jet deposition in melt impouring jet deposition equipment is become to billet;
5) go end face to carry out crimp processing in the billet railway carriage after above-mentioned jet deposition;
6) follow the bar that distortion bar is cut into long 150mm, carry out solution treatment after railway carriage, solid solution treatment process is: 440～460 DEG C of 50～70min+465～485 DEG C 1.5～2.5h, carry out room temperature shrend afterwards;
) aluminum alloy materials after quenching is put into furnace temperature is the baking oven of 70 DEG C-80 DEG C, place 240h～360h and carry out manual intervention natural aging treatment.
As preferably, described step 3) add-on of refining agent and alterant accounts for the 0.4-0.6% of melt quality.
As improvement, described step 3) also to skim to melt after rotten and refining treatment, afterwards melt is left standstill to 10min-15min, melt temperature is risen to 800 DEG C-830 DEG C in order to spray deposition technology.
As improvement, described step 4) concrete technology of jet deposition is: atomizing pressure is 0.5-0.7MPa, and sweep rate is 23.0～24.0HZ, and sediment pan rotation frequency is 3.15-3.20HZ, it is 270-300mm that melt is deposited as to diameter, is highly greater than the billet of 300mm.
As improvement, described step 5) the technique of crimp be: billet is heated to 380 DEG C-420 DEG C, carries out crimp processing on 3000t indirect extrusion machine, extrusion ratio is 8.5～9.5:1.
As preferably, described step 6) solid solution treatment process be: 450 DEG C of 1h+475 DEG C of 2h.
Preferred again, described step 7) the manual intervention natural aging treatment time be 360h.
The feature of natural aging is that its intensity and plasticity all keep higher level, when reason is to adopt natural aging technique, when aging time is sufficient, separates out even tiny G.P district and MgZn in the crystal grain inside of alloy
2' phase, the intensity of this tissue distribution alloy and plasticity toughness have compared with favorable influence.If employing artificial aging, due to separating out to all changing MgZn into of crystal grain inside
2' phase or MgZn
2phase, the tensile strength of alloy increases, but has but significantly reduced plasticity and the toughness of alloy.The good over-all properties of alloy wishes significantly to shorten again the time Te Famingben aging technique of natural aging simultaneously when obtaining natural aging, is called manual intervention natural aging.
Compared with prior art, the invention has the advantages that: adopt spray deposition technology to be prepared, alloying element comprises that micro-total content exceedes 16%, alloy is after strengthened solution, change traditional natural aging treatment, and adopt the ageing treatment through 240h-360h at 70 DEG C-80 DEG C, so not only greatly reduced natural aging time, and alloy property is better; Adopt spray deposition technology not only to increase the solid solubility of aluminium alloy interalloy element, in the time of follow-up timeliness, improved timeliness power, improved the mechanical property of alloy, make the ultra-high-strength aluminum alloy homogeneous microstructure of development simultaneously, tiny, there is not macrosegregation.Ultra-high-strength aluminum alloy grain-size of the present invention is between 4-6um, alloy material is after manual intervention natural aging, its properties is that tensile strength is between 780MPa-820MPa, yield strength is between 700MPa-740MPa, unit elongation has reached between 9%-13%, and fracture toughness property is at 30-35MPam
1/2between, its over-all properties has reached international most advanced level, has improved production efficiency simultaneously.
Brief description of the drawings
Fig. 1 is jet deposition ultra-high-strength aluminum alloy deposited tissue in the embodiment of the present invention 1;
Fig. 2 is jet deposition ultra-high-strength aluminum alloy As-extruded tissue in the embodiment of the present invention 1;
Fig. 3 is jet deposition ultra-high-strength aluminum alloy quenching state tissue in the embodiment of the present invention 1;
Fig. 4 is tissue when jet deposition ultra-high-strength aluminum alloy room temperature natural aging state 360h in the embodiment of the present invention 1;
Fig. 5 is tissue when jet deposition ultra-high-strength aluminum alloy manual intervention natural aging state 240h in the embodiment of the present invention 1;
Fig. 6 is tissue when jet deposition ultra-high-strength aluminum alloy manual intervention natural aging state 360h in the embodiment of the present invention 2.
Embodiment
Below in conjunction with accompanying drawing, embodiment is described in further detail the present invention.
Embodiment 1
Take respectively 84.2kgAl, 12kgZn, 2.4kgMg, 1.0kgCu, 0.2kgZr, 0.1kgMn, 0.1kgNi puts into stove melting, wherein Cu adopts Al-50Cu master alloy, Ni adopts Al-20Ni master alloy, all the other are pure metal, fusion process is: the above-mentioned alloy weighing up is comprised to Al, Al-50Cu master alloy, Al-Ni master alloy is put into medium-frequency induction furnace, energising adds until the metal in crucible dissolves, when being risen to 720 DEG C-740 DEG C, melt temperature adds Zr particle and pure Mn sheet, after fully stirring, melt temperature is risen to 800 DEG C-820 DEG C, after power-off, adopt graphite to press spoon to be pressed into pure Zn and pure Mg, fully stir, melt temperature is risen to 720 DEG C-750 DEG C, adopt refining agent and alterant (weight percent 0.5%) and C
2cl
6degasifier goes bad and refining treatment to melt.After processing, melt is skimmed, afterwards melt is left standstill to 10min-15min, melt temperature is risen to 800 DEG C-830 DEG C in order to spray deposition technology; By in melt impouring jet deposition equipment, wherein atomizing pressure is 0.5-0.7MPa, and sweep rate is 23.4HZ, and sediment pan rotation frequency is 3.15-3.20HZ, and it is 270-300mm that melt is deposited as to diameter, is highly greater than the billet of 300mm; The injection deposition blank ingot car skin of development is removed to end face, billet is heated to 380 DEG C-420 DEG C, carry out crimp processing on 3000t indirect extrusion machine, extrusion ratio is 9:1; The bar that is cut into long 150mm at distortion bar, carries out solution treatment after railway carriage, solid solution treatment process is: 450 DEG C of 1h+475 DEG C of 2h, carry out room temperature shrend afterwards; It is the baking oven of 70 DEG C-80 DEG C that aluminium alloy after quenching is put into furnace temperature, and be 240h storage period, another batch of aluminium alloy is placed on to room temperature simultaneously and carries out room temperature natural aging treatment.Aluminium alloy material is carried out to tension specimen processing according to GB, finally carry out Mechanics Performance Testing.
The microtexture that wherein Fig. 1 is its deposited, Fig. 2 is jet deposition ultra-high-strength aluminum alloy As-extruded tissue, Fig. 3 is jet deposition ultra-high-strength aluminum alloy quenching state tissue, tissue when Fig. 4 is jet deposition ultra-high-strength aluminum alloy room temperature natural aging state 360h, tissue when Fig. 5 is jet deposition ultra-high-strength aluminum alloy manual intervention natural aging state 240h.
As can be seen from the figure, in the deposited tissue of ultra-high-strength aluminum alloy, have micropore and pore, this is because spray deposition technology natural characteristics determines, the grain-size of deposited, between 5-10um, exists the second-phase of separating out in tissue.From As-extruded tissue, can find out,, there is not dynamic recrystallization in tissue fibroblast shape after billet distortion.From quenching state tissue, can find out, alloy is after quenching, and in tissue, except thick second-phase, all the other tiny precipitated phases all solid solution enter in alloy substrate, illustrate that this solid solution craft meets heat treatment requirements.From the alloy structure of manual intervention natural aging 240h, can find out, in alloy structure crystal grain, separated out and tiny gathering phase or second-phase, this tissue is called G.P district, and just because of the existence of this phase, the intensity of alloy is just greatly improved.From the tissue of room temperature natural aging state, can find out, although the time of room temperature natural aging is longer than manual intervention natural aging time, this tissue Zhong G.P district is little, far fewer than the alloy structure of manual intervention natural aging 240h.
Above two kinds of alloy materials are carried out to mechanics property analysis, and result shows that its tensile strength of alloy, yield strength, unit elongation and the fracture toughness property of room temperature natural aging are respectively 745MPa, 675MPa, 8.5% and 28MPam
1/2, and tensile strength, yield strength, unit elongation and the fracture toughness property of manual intervention natural aging alloy are respectively 790MPa, 705MPa, 9.5% and 32MPam
1/2, the alloy property of therefore manual intervention natural aging is better than the alloy of room temperature natural aging.
Embodiment 2
Take respectively 79.9kgAl, 14kgZn, 3.2kgMg, 1.5kgCu, 0.5kgZr, 0.3kgMn, 0.6kgNi puts into stove, wherein Cu adopts Al-50Cu master alloy, Ni adopts Al-20Ni master alloy, all the other are pure metal.Complete starting material melting according to the step in embodiment 1, billet moulding, billet machining deformation, Aluminium Alloy Solution Treatment and manual intervention natural aging treatment, the wherein manual intervention natural aging treatment time is respectively 360h and 480h.Tissue when Fig. 6 is jet deposition ultra-high-strength aluminum alloy manual intervention natural aging state 360h.
As can see from Figure 6, in the tissue of manual intervention natural aging 360h, there is a large amount of GP district, also occur MgZn simultaneously
2(η ') phase, the appearance of this phase can make the properties of this alloy reach peak value.The alloy of above two kinds of aging times is carried out to mechanics property analysis, and result shows that tensile strength, yield strength, unit elongation and the fracture toughness property of manual intervention natural aging 360h alloy are respectively 820MPa, 740MPa, 13% and 35MPam
1/2, tensile strength, yield strength, unit elongation and the fracture toughness property of manual intervention natural aging 480h alloy are respectively 815MPa, 720MPa, 12.7% and 34MPam
1/2, can find out, its over-all properties of alloy of manual intervention natural aging 360h has reached the best, continues to extend its mechanical property of aging time and declines to some extent.
The alloy of quenching state is carried out to room temperature natural aging treatment, and aging time is respectively 1 month, and 3 months, 6 months, 1 year, its tensile strength was respectively 750MPa, 765MPa, 780MPa and 818MPa; Yield strength is respectively 680MPa, 685MPa, 695MPa and 715MPa; Unit elongation is respectively 8.5%, 9.2%, and 11% and 12.5%; Fracture toughness property is respectively 28MPam
1/2, 29MPam
1/2, 32MPam
1/2, 35MPam
1/2.
Claims (8)
1. a ultrahigh-strength aluminum alloy material, is characterized in that: the mass percent of the concrete composition of this aluminum alloy materials is Zn:12%-14%; Mg:2.4%-3.2%; Cu:1.0%-1.5%; Zr:0.2%-0.5%; Mn:0.1%-0.3%; Ni:0.1%-0.6%; Surplus is Al.
2. a preparation method for ultrahigh-strength aluminum alloy material, is characterized in that comprising the following steps:
1) per-cent that weighs is Zn:12%-14%; Mg:2.4%-3.2%; Cu:1.0%-1.5%; Zr:0.2%-0.5%; Mn:0.1%-0.3%; Ni:0.1%-0.6%; Surplus be the material of Al as the starting material of this alloy, wherein Cu adopts Al-50Cu master alloy, Ni adopts Al-20Ni master alloy, all the other are pure metal;
2) the above-mentioned alloy raw material Al weighing up, Al-50Cu master alloy, Al-Ni master alloy are put into medium-frequency induction furnace, energising adds until the metal in crucible dissolves, when being risen to 720 DEG C-740 DEG C, melt temperature adds Zr particle and pure Mn sheet, after fully stirring, melt temperature is risen to 800 DEG C-820 DEG C, after power-off, adopt graphite to press spoon to be pressed into pure Zn and pure Mg, fully stir, melt temperature is risen to 720 DEG C-750 DEG C;
3) adopt refining agent and alterant and C2Cl6 degasifier to go bad and refining treatment to melt;
4) jet deposition in melt impouring jet deposition equipment is become to billet;
5) go end face to carry out crimp processing in the billet railway carriage after above-mentioned jet deposition;
6) follow the bar that distortion bar is cut into long 150mm, carry out solution treatment after railway carriage, solid solution treatment process is: 440～460 DEG C of 50～70min+465～485 DEG C 1.5～2.5h, carry out room temperature shrend afterwards;
7) aluminum alloy materials after quenching being put into furnace temperature is the baking oven of 70 DEG C-80 DEG C, places 240h～360h and carries out manual intervention natural aging treatment.
3. preparation method according to claim 2, is characterized in that: described step 3) add-on of refining agent and alterant accounts for the 0.4-0.6% of melt quality.
4. preparation method according to claim 2, it is characterized in that: described step 3) also to skim to melt after rotten and refining treatment, afterwards melt is left standstill to 10min-15min, melt temperature is risen to 800 DEG C-830 DEG C in order to spray deposition technology.
5. preparation method according to claim 2, it is characterized in that: described step 4) concrete technology of jet deposition is: atomizing pressure is 0.5-0.7MPa, sweep rate is 23.0～24.0HZ, sediment pan rotation frequency is 3.15-3.20HZ, it is 270-300mm that melt is deposited as to diameter, is highly greater than the billet of 300mm.
6. preparation method according to claim 2, is characterized in that: described step 5) the technique of crimp be: billet is heated to 380 DEG C-420 DEG C, carries out crimp processing on 3000t indirect extrusion machine, extrusion ratio is 8.5～9.5:1.
7. preparation method according to claim 2, is characterized in that: described step 6) solid solution treatment process be: 450 DEG C of 1h+475 DEG C of 2h
8. preparation method according to claim 2, is characterized in that: described step 7) the manual intervention natural aging treatment time be 360h.
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Cited By (9)
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| CN105648290A (en) * | 2016-03-15 | 2016-06-08 | 昆明理工大学 | High-strength aluminum alloy and preparation method thereof |
| CN106623465A (en) * | 2016-12-29 | 2017-05-10 | 山东诺维科轻量化装备有限公司 | Production method of railway vehicle electrical cabinet aluminum profile |
| CN107675112A (en) * | 2017-10-12 | 2018-02-09 | 哈尔滨工业大学 | A kind of jacket deformation method of ultra-high-strength aluminum alloy |
| CN109158604A (en) * | 2018-09-11 | 2019-01-08 | 湖南工业大学 | A kind of aluminium alloy shell case manufacturing method and shell case |
| CN109161745A (en) * | 2018-10-23 | 2019-01-08 | 苏州杰森电器有限公司 | A kind of grass-mowing machine strong mechanical performance aluminium alloy and its manufacturing method |
| CN110684913A (en) * | 2019-10-12 | 2020-01-14 | 中国兵器科学研究院宁波分院 | Preparation method of ultrahigh-strength and high-toughness aluminum alloy |
| CN111074124A (en) * | 2020-01-22 | 2020-04-28 | 中南大学 | Thermomechanical treatment composite process for 7xxx aluminum alloy uniform structure and obtaining method thereof |
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| CN106623465A (en) * | 2016-12-29 | 2017-05-10 | 山东诺维科轻量化装备有限公司 | Production method of railway vehicle electrical cabinet aluminum profile |
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| CN111074124A (en) * | 2020-01-22 | 2020-04-28 | 中南大学 | Thermomechanical treatment composite process for 7xxx aluminum alloy uniform structure and obtaining method thereof |
| CN111487129A (en) * | 2020-04-16 | 2020-08-04 | 江苏豪然喷射成形合金有限公司 | Method for testing room-temperature tensile mechanical properties of 7055 ultra-high-strength aluminum alloy extruded material formed by spraying |
| CN113146149A (en) * | 2021-03-29 | 2021-07-23 | 中信戴卡股份有限公司 | Method for producing special vehicle wheel by applying 7000 series aluminum alloy |
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