CN1060115A - Be suitable for making the aluminium alloy of jar - Google Patents
Be suitable for making the aluminium alloy of jar Download PDFInfo
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- CN1060115A CN1060115A CN91108893A CN91108893A CN1060115A CN 1060115 A CN1060115 A CN 1060115A CN 91108893 A CN91108893 A CN 91108893A CN 91108893 A CN91108893 A CN 91108893A CN 1060115 A CN1060115 A CN 1060115A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- 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
Abstract
The invention describes a kind of aluminium pot material, it has the intensity higher than traditional aluminium pot material, ductility and anisotropy preferably.This aluminium pot material is by following alloy manufacturing, 3.0 the zinc of-8.0 weight percents, the magnesium of 0.5-3.0 weight percents is less than the iron of 0.7 weight percent, 0.01 the silicon of-2.0 weight percents, 0.05 the copper of-0.9 weight percent, the manganese of 0.1-11 weight percents is less than the chromium of 0.3 weight percent, impurity is less than 0.15 weight percent, and in these aluminium alloys, zirconium is not impurity usually, and preferably its content is less than 0.01 weight percent.
Description
The present invention relates to make the application of the aluminum base alloy of fluid container, particularly be suitable for the high zinc aluminium base alloy of liquid-container structure.
Traditional split type aluminum beverage container is usually by two kinds of different alloy manufacturings, for example 3004 of ABAL's standard and 5182 type alloys (seeing Table 1).3004 type aluminium alloys are made tank body through the manufacturing process of the ironing of deep draw and wall usually, but it does not have the cover material required just, strength characteristics, and 5182 type alloys are not suitable for tank body, only have cover and make required characteristic.To the increase of the demand of this type of container and to thinner more blocky jar demand, stimulated the development of new alloy, furtherly, stimulated the development that can be used for the alloy of tank body and cover raw material simultaneously.
The alloy that is applicable to tank body must have good formability and high-intensity over-all properties and be economical on making.
The alloy of the AA of Aluminum Company of America 3004 type alloy components uses DC-casting (DC-Cast) traditionally, be cast as that section is thick as 500mm, the ingot bar of 700mm about wide, then, ingot bar was 500-620 ℃ of following homogenizing 4 to 24 hours, and hot rolling, by a series of roughing mill train, course of hot rolling makes the thickness of ingot bar reduce to 2-3mm.
Usually, material through 0.5-4 hour annealing, makes the metal recrystallization under 300-400 ℃ of temperature.The annealed metal again through cold-rolled process improving intensity and other characteristic, this is generally by 2-5 mill train, the economy of 20-50% at every turn finally becomes the thickness of 0.3-0.33mm.
Final material is made aluminium pot through drawing press and tank body jointing machine.Under the disk of about 135mm diameter on the drawing press is sheared from the cold-working plate or sweep away and pull and stretch becomes shallow cup.This cup enters a jar jointing machine again, and pull and stretch becomes the cup near its final diameter at first again.The wall of cup is through one or many ironing operation, and thickness reduces, and makes the diameter about 65mm at last, 140mm height, the tank body of 0.10-0.18mm wall thickness.
The material of above-mentioned tank body pull and stretch has anisotropy (being that characteristic has nothing in common with each other) on all directions, the top of pull and stretch tank body has burr, forms four spikes that differ 90 ℃ of intervals approximately, and this spike is called as " ear shape projection ".The degree of ear shape projection can be determined with following formula on letter ground:
2 (he-ht)/(he-ht) * 100=% ear shape projectioies
Here: he be glass at the bottom of to the distance on ear shape projection pinnacle;
Ht be glass at the bottom of to the distance of the sharp paddy of ear shape projection;
The tank body that further can be processed into beverage container must be less than the ear shape degree of convexity of 3-5%, and preferably less than 3%, in the process of incision operation, with upper end (by the fixed one procedure) deflashing of tank body, " ear shape projection " district goes out of use.
To other consideration of the tank body quality finished is non-cracked crystallized ability and have final level and smooth surface in the tank body jointing machine, do not have to draw and scratch or ordinate, if this material does not have suitable microstructure, " scratch " (galling) causes deep trouth to occur on the tank skin that has been shaped.
In order to reduce the cost of tank body, shallow (the Domn gauging) of common strain hardening alloy needs (for example to increase alloying element, copper, manganese, magnesium) content, to gain in strength, yet, increase with these content, the formability of final alloy reduces, in fact, 3 * * * series alloy strength Bi Jing be subjected to the rolling deformation quantitative limitation, this amount is in the profiled surface and the prerupture course of processing of material behavior, the amount that material can bear, now other aluminum alloy system of other application usefulness can reach than 3 * * * strength level that series alloy is higher.
After all, container can be made by the high strength 3004 type Alloy Forming of the attenuate manufacturing with nothing adhesion (galling), the little characteristic of ear shape projection, unless this intensity is high enough to compensate the loss of strength that wall thickness reduces, the buckling resistance of jar can reduce.
Buckling strength or buckling resistance depend on the pressure in the jar that puts on pull and stretch and wall ironing, gradually pressure boost until tank bottom deformation, bloat, promptly buckle or inverted circular arch is routed up, the pressure when buckle in the bottom is defined as buckling strength or arch counterpressure (dome reversed pressure).By the acceptable jar tank body of alloy material manufacturing the buckling strength that must have be at least 85 pounds/cun
2Use common DC-casting (D.C method), the can that is drawn by high-strength 3004 alloys has 90 pounds/cun
2About buckling strength.
Generally adopt though produce 3004 tank body blanks with the ingot casting, and would rather make aluminium sheet by continuous metal cast process from the consideration of the economy and the energy, prior art has been advised with being with casting method continuously.This moment, aluminium was cast the thin alloy band of about 1 inch thickness, use this technology treating processes that homogenizes to save, the economy that is hot-rolled down to intermediate gauge is reduced to minimum, if reach required microtexture in the continuous casting process of strip, course of hot rolling also can save fully.In the mode of similar processing ingot casting material material is carried out anneal then.So far, proved that for further processing and tank body manufacturing, the jar blank made with this method be unsafty.
Like this, an object of the present invention is to provide a kind of aluminium alloy that is suitable for doing jar blank, it has than existing AA 3004 type alloys at least and does not have adhesion, low " ear shape " protruding performance, high-strength characteristic, superior formability, it makes tank body by thin blank plate manufacturing.Another purpose of the present invention is to provide and is suitable for the jar blank that cover is made equally, makes the beverages can of split type close manufacturing by a kind of gold of composition fully.No matter this alloy is suitable for by DC-casting or is with casting continuously, all can manufacture a jar blank.Further, the technology that the present invention relates to a kind of jar of blank and produce jar blank from the aluminium alloy of following composition, this alloy comprises 3.0-8.0%(weight) zinc, 0.5-3.0%(weight) magnesium, less than 0.7%(weight) iron, 0.01-2.0%(weight) silicon, 0.05-0.9%(weight) copper, 0.1-1.1%(weight) manganese and 0.0-0.3%(weight) chromium.Other impurity is less than the 0.15%(weight of gross weight in the alloy) level.
According to a further aspect in the invention, the technology for the system jar blank that the production line supply is required, processing alloy comprises:
Melt the alloyed metal that is suitable for casting,
It is cast as be suitable for rolling shape,
Be rolled to intermediate gauge in finishing,
This alloy of thermal treatment,
Cold rolling in the economy scope of 2-85%, this is the last operation of rolling;
The tempering heat treatment material to the ductility that needs and intensity.
This alloy preferably has the composition of following weight percentage ranges: zinc 4.0-6.5, and magnesium 1.0-2.5, manganese 0.3-0.8, silicon 0.15-0.3, iron height to 0.45, copper 0.10-0.5, chromium height to 0.2, other total impurities is less than 0.1.When containing zirconium amount height in the alloy, can be suitable for system jar blank to highest level 0.25% weight ratio, have little " ear shape " ridge when making tank body, preferred zirconium content is less than 0.08%(weight), most preferredly in melting liquid, do not add, its content is lower than the content of impurity, i.e. 0.1% weight ratio.
Have been found that the alloy that falls into above-mentioned composition range reaches high tensile and yield strength characteristic, and the nothing of good formability and wall adhesion ironing quality.This alloy is suitable for making beverage tank body and cover most.
This alloy can be made above 90 pounds/cun
2The tank body of the anti-intensity of arch, and the wall thickness behind the ironing is less than 0.16mm.A3004 type alloy when wall thickness is equal to or greater than 0.16mm, can only reach so anti-intensity of arch usually.
Above-mentioned alloy can be suitable for rolling with DC-casting, continuously casting and be with the casting manufacturing continuously.Yet if alloy uses rolling or the manufacturing of band casting method, the scope of its component can be relaxed.
The content of zinc (Zn), magnesium (Mg), manganese (Mn), iron (Fe) and silicon (Si) can increase, and they cause the α phase particulate of high volume percentage after casting, causes in last operation to deposit in a large number.
In the end in the manufacturing in stage, by rolling thin and combined with heat treatment can the alloying plate.Certainly, manufacturing processed changes with the needs of final use.Yet, in the heat treatment operation process, have been found that the alloy of formation is particularly suitable for the solution heat treatment of very short process, and can be used to use the annealing of the plate of full annealed or reduced anneal technology than the thermal treatment of growth process simultaneously.
Be used for structure of container or other requirement, intensity and formability are important, ingot or band casting material can thermal treatment with the homogenizing cast material, and preferably cold rolling after the hot rolling.Then, material for improving intensity and ductility, depends on the needs of final use through solution heat treatment and cold rolling thin, last, and alloy is carried out the timeliness tempering.
Best, cast material, ingot casting for example must be through the equal alloy of further heat treatment step, and preferably follows through after the hot-rolled step.
The rolling preferably cold rolling step of intermediary in the cold rolling manipulation process, can adopt the process annealing of comprehensive annealing or timeliness.
The preferably solution heat treatment of heat treatment of alloy step can be carried out after the timeliness step.
Last rolling step is absolutely necessary for purposes of the invention, and is same to provide the finished product essential strength characteristics, must guarantee to be suitable for making the enough ductility and the formability of tank material.Finish to gauge is that the economy scope is the cold rolling of 2-85%, and preferably scope is 10-80%, and optimized scope is 30-80%, and final tempering heat treatment is artificial aging preferably.
According to further aspect of the present invention, the jar production line of being made by alloy of the present invention is provided and supplies with material, it preferably has above the surrender of 400MPa and tensile strength and 4% or bigger breaking elongation.
Alloy of the present invention also can be used for making a system jar final blank, and this material must have the yielding stress of minimum 310MPa under Annealed Strip, the tensile stress of the lower limit of 355MPa and minimum 6% unit elongation.
More than the intensity of final blank of the jar of regulation and unit elongation relate to material after bake intensity.
Usually, whole blank is made web form, send into the end jointing machine, the coating plate also toasted coating 10-30 minute under temperature suitable between 155 ℃-210 ℃, usually, the test of above-mentioned materials is to dry by the fire 20 minutes down at 205 ℃, then, with traditional metal working process manufacturing, those skilled in the art knows this technology by the end jointing machine of jar for jar end.
When jar end constructed in accordance after the state of baking have the above-mentioned minimizing intensity and the ductility of surpassing, suitable jar end can be made by alloy of the present invention.
Another aspect of the present invention is the beverage container of the split type made by alloy of the present invention, and the best wall thickness of this container encircles anti-intensity greater than 90 pounds/cun less than 0.12mm
2
The present invention's purpose and advantages aforementioned and other characteristics are clearer by following preferred embodiment and corresponding accompanying drawing briefing.
Table 1 comprises the scope and the preferable range of alloy each several part of the present invention;
Fig. 1 is a schema of representing the whole making processes of alloy in detail;
Fig. 2 is a differential scanning calorimeter curve of alloy of the present invention.
Fig. 3 (a) is the schema of the final stage of alloy manufacturing;
Fig. 3 (b) has represented the effect of last cold rolling attenuate;
Fig. 3 (c) has represented the cold working and the artificially aged effect of embodiment 1 interalloy;
Fig. 4 represents that embodiment 2 interalloies 2 are in the micro-photograph in each process segment, wherein:
Fig. 4 (a) is the microstructure of material after the hot rolling;
Fig. 4 (b) is the microstructure of annealing back material;
Fig. 4 (c) is the microstructure of material behind the last cold rolling attenuate.
Fig. 5 illustrates the artificially aged effect of embodiment 2 interalloies 1,2,3.
Fig. 6-the 8th, each alloy and time relation curve among the embodiment 2 of final timeliness at a certain temperature;
Fig. 9 shows the natural aging of alloy and cold worked effect;
Figure 10 is illustrated in effect and the cold worked effect of using two temperature to handle in the artificial aging step;
Figure 11 is the tension result of alloy of the present invention;
Figure 12 has represented the intensity of alloy of the present invention and the comparison of ductility and traditional 3004 type jar raw materials.
Figure 13 has summarized the advantage of alloy of the present invention.
Alloy of the present invention comprises following basic alloy element (percentage by weight): copper (0.05-0.9), manganese (0.1-1.1), magnesium (0.5-3.0), and relatively high zinc content (3.0-8.0). Further, following component is included in the melt: chromium (0.0-0.30), silicon (0.1-2.0), iron (0.0-0.5).
Have been found that through solution heat treatment most magnesium and zinc suspension deposit in solid solution, increase the needed intensity of alloy when tempering heat treatment.
The silicon of above-mentioned scope, manganese and ferrous components are essential to the present invention, because, above-mentioned element, the dispersion that is used to form second-phase in the needed alloy (α phase) distributes, and this point is important for the stretching that tank skin does not have adhesion.
Find uniquely, zirconium and chromium only have the impurity content less than 0.01% weight ratio in melt, if they have existed in melt or for extra strength characteristics adds them, preferably their content is respectively less than 0.08% and 0.05% weight ratio.
Refining chromium and the very low-grade granularity role of better zr element be, after for example hot rolling or process annealing (345 ℃ lasting 0.5-2 hour), product produces completely recrystallization.
If zirconium and the chromium content in alloy surpasses the above-mentioned scope of the present invention, the forging structure that produces when heat, cold rolling can keep when solution heat treatment or annealing in process, the sheet material of last specification can have anisotropy, this carries out deep-drawing to this sheet material, and to add man-hour very unfavorable,, anisotropy is unsuitable for the procedure of processing of tank body because causing height " ear shape " the protruding characteristic of material, the alloy that increases above element can obtain high strength, but formability descends and bad ear shape projection.
The yield strength of alloy of the present invention and tensile strength is far above the serial tank body material of 3XXX, and this 3004 alloy has respectively 285 and the surrender of 330MPa and the percentage elongation of tensile strength and 4%. And alloy of the present invention has respectively 420 and surrender, the tensile strength of 480MPa, and to the measurement of 50mm full-length, its breaking elongation is more than 4%. When this Sheet drawing and ironing wall were made tank body for amalgamation or container for drink, it had above 100 pounds/cun when the 0.12mm wall thickness2The buckling strength of tank. This alloy have than any 3004 types or improved 3 * * * the higher intensity of series alloy and the toughness of improvement, this so that be used for the buckling strength of thickness tank body after guaranteeing to be shaped of plate of preliminarily forming operation (feeding of tank body production line) and formability under be reduced by at least 10%.
The high strength of this alloy also makes it be used for the manufacturing of the lid base of tank, and the AA5182 alloy that is generally used for the cover making has the tensile strength of 395MPa and 4% percentage elongation. Owing to there is not enough intensity under the thickness of required lid, 3004 type alloys are unsuitable for making cover usually, and alloy of the present invention can reach the characteristic of AA5182 alloy, and this split type tank can be by a kind of alloy component manufacturing, rather than common two kinds.
When alloy casts to make tank body by DC-casting, its processing that at first should homogenize. Foundry goods preferably is used as blank and was homogenized 5-10 hour at 480 ℃-500 ℃, and material is hot-rolled down to the thickness (preferably less than 5mm) that is fit to coiled material under the temperature of height to 500 ℃ then. Preferably the final temperature of coiled material hot rolling is higher than about 300 ℃, and alloy can be annealed when reeling automatically like this.
Material is cold rolling then, and is preferably in cold rolling middle adopt comprehensively annealing or reduced anneal. Through this rolling sequence, the band material preferably has the thickness of 0.8-0.4mm. For finishing rolling economy at the finishing operation of tank shell material processed, with Pingdu that necessary plate is provided and last thickness of slab intensity, above thickness needs.
Subsequent, to room temperature, between best 480 ℃ and 595 ℃, carry out 5 seconds to 1 hour solution heat treatment in water-cooled.
If cold rolling mistake is carried out solution heat treatment in the upper limit of processing time scope and also can be made anneal of material in advance. But, the composition of alloy so that the heat treatment time of material than the used time much shorter of common 3004 alloys.
Alloy strip steel rolled stock can carry out the timeliness under the room temperature then, and preferably cold rolling before timeliness is 0 to 48 hour.
For providing metal essential strength characteristics, cold rolling economy scope is that 2-85% is necessary in the finish to gauge step, preferred economy is 10-80%, that optimum is 30-70%, have been found that, even cold rolling economy is got the upper limit of this scope, material has the available necessary ductility of tank blank and machinability.
Last plate between lack time effect and overaging state, the timeliness tempering. Timeliness depends on used device and tank producer's intensity and the standard of ductility. Be preferably in 120-260 ℃ the scope timeliness 1 minute-4 hours.
To the solution heat treatment of the material last heavy lattice chemical industry order early than material, reduce the anisotropy that the cold rolling stage produces, this means that made deep-drawing material has low anisotropy and low-down ear shape degree of convexity in order to give the required degree of temper of last rolling calendering and comprehensive timeliness. With 3004 or typically improve alloy and have 3% ear shape degree of convexity. The cup of alloy made of the present invention has and is less than 2% ear shape degree of convexity.
At traditional alloy with the casting of casting machine band near one inch or can replace the material of DC-casting gained less than the band of an inch thickness, supplying with alloy blank with casting of obtaining of this method can be more than the alloy composition of direct pouring, but preferably has alloys range of the present invention (seeing Table 1). Then, the band material is extended down to minimum 25% through heat or cold rolling, the plate of the economy of better 50%-85% thickness.
Alloy component of the present invention and processing technology make the liquid container wall can be by thin sheet material manufacturing, and reduce cost. Further, a kind of alloy can be used for the tank body blank by the step that changes alloy processing, end blank and pull-tab blank.
Be used for the use of single alloy model of whole parts of liquid container, so that produce the benefit of processing price and improved the recycling of scrap.
Following embodiment introduces alloy of the present invention.
Embodiment 1: following is by the alloy component (weight %) of direct chill casting to 50cm * 120cm specification ingot:
Zinc-magnesium iron copper silicon manganese chromium aluminium
4.83 1.53 0.35 0.16 0.019 0.47 0.01 all the other
Ingot is produced the sheet material of reeling through following operation.
-under 480 ℃-595 ℃, homogenize and handled 5 hours;
-be hot-rolled down to 3.175mm,
295-315 ℃ of roll bending outlet measuring temperature,
Through the standard deburring;
-annealed 3 hours down at 370 ℃-373 ℃;
-be cold-rolled to 1.22mm by 60% economy;
-solution heat treatment under 1.22mm thickness;
Molten 10 seconds of 585 ℃ of following flash;
-cold rolling 40% economy is to thickness of slab 0.73mm,
Be cold-rolled to thickness of slab 0.454mm with 37% economy again,
Economy with 35% is cold-rolled to thickness of slab 0.303mm;
-leveling, solvent is washed sheet material;
-artificial aging is to the T87 degree of temper
160 ℃ of following timeliness one hour.
In the above-mentioned stage, in case through Overheating Treatment, coiled material is rolled to last thickness at back-to-back mill train, and before beginning was rolling, multipotency postponed 48 hours.
The planted agent carried out leveling in cold rolling back 5 days, to avoid undue natural aging, because the timeliness of cold rolling back material can increase hardness.
The testing mean of 50 samples is as follows:
Yield strength 393MPa;
Ultimate tensile strength 406MPa;
Ductility 4.34mm;
The made tank body of sample has shown 0.30mm buttress thickness, and the arch counterpressure is 105 pounds/cun
2Fig. 3 (b) has shown the intensity of the involutory gold of last cold rolling calendering and the influence of ductility, Fig. 3 (c) points out that alloy material delays the influence of artificial aging time to intensity and ductility in solution heat treatment (S.H.T) and 70% cold rolling, and aging temp is 250 °F (121 ℃).
The ingot bar of finishing is cooled to 500-485 ℃ rolling temperature in stove, so that this alloy of hot rolling, ingot bar shifts out from stove subsequently, and thick from the thick rolling last about 2-3mm of 100mm respectively, the microstructure of hot-finished material is shown in Fig. 4 a.
The hot rolled outlet temperature often is higher than 200 ℃.This temperature is enough to allow some recovery of structure that has been rolled before being cold-rolled to solution heat treatment thickness, yet, in the situation of some alloy sample 3, material under 345 ℃ of temperature through 3 hours full annealed.This recovers and recrystallization material comprehensively, and the mean diameter of the crystalline size of the complete recrystallization of alloy is 19 μ m(American Standard of Testing Materials ASTM 8.5) (seeing Fig. 4 b).
Under this softening condition, many different thickness that the cold rolling one-tenth of alloy table 4 is shown.This is to be convenient under the situation of many final cold rolling economies that do not wait, and makes to be used for the given sheet material of final thickness that the tank body blank is made, above-mentioned.Fig. 3 a has shown the operation that material is final.
Fig. 4 (c) has shown the microstructure of delaying sample 2 interalloies 2 through last cold rolling, from Photomicrograph as can be seen, all is dispersed with α phase (α-Al(Fe, Mn) Si in the material matrix).This microstructure is illustrated in the ironing of wall, and tank body has good nothing adhesion index.
Carry out the solution heat treatment of plate under 500 ℃ of temperature, the last timeliness step that makes element enter solute is prepared.Three kinds of alloys are shown in Fig. 5 in the natural aging The Characteristic Study of 500 ℃ of following solution heat treatment after 2 hours, and material carries out a series of thermal treatment then through cold-water quench, and aging research and hardness measurement are used to represent the reaction of alloy to different treatment.Yield strength and the unit elongation of sheet material tension test under certain condition to determine that specific alloy is handled.
The analysis of final ageing treatment is shown in Fig. 6-8.
Fig. 6 (a) 6(b), 6(c) is illustrated respectively in for the first time 121 ℃ of timeliness after 1,2,3 hours, the rational curve of alloy during timeliness under 155 ℃.
Fig. 7 (a), 7(b), 7(c) be illustrated respectively in natural aging aging characteristic curve at 111 ℃ of following alloys after 0,24,48 hours.
Fig. 8 (a), 8(b), 8(c) be illustrated respectively in natural aging aging characteristic curve at 131 ℃ of alloys after 0,24,48 hours.
Table 4
Fig. 9 represents the effect cold rolling to alloy 2.
Figure 10 (a) and 10(b) shown that cold-working (CW) at 0-60% handles back alloy 2 materials and carry out the artificially aged effect second time, the alloy of Figure 10 (a) is through 500 ℃ of solution heat treatment of 2 hours, 0 hour natural aging continues 3 hours in 121 ℃ of cold-workings and consistent artificial aging.At Figure 10 (c), this alloy is through 500 ℃ of solution heat treatment of 2 hours, 48 hours natural aging, cold-working and under 121 ℃ the preceding artificial aging continue 3 hours.
Table 4 has shown cold-working and the multiple effect of the artificially aged influence to embodiment 2 alloys 1,2,3.
The hurdle of sign CW is illustrated in the economy per-cent of cold-working step.AA(1) and AA(2) hurdle is with the T/t formal specification, and T is the centigradetemperature of heat treatment step here, and t is the time hours that material keeps in this temperature.
Natural aging time is represented on the hurdle of sign NA, and SHT/ANN is solution heat treatment/artificial aging steps A A(1) and AA(2) represent the annealed temperature and time in the mode of T/t.Remaining hurdle is respectively yield strength, ultimate tensile strength, unit elongation, " ear shape " projection and arch counterpressure.
For the manufacturing of tank body and the measurement of " ear shape " degree of convexity, make cup with many sheet material alloys, cup closes at tank body and is shaped as tank body on the machine, and the result of each test specimen is atresia or does not have the tank body that the success of trace is drawn on the surface.Selected jar buckling resistance is tested on traditional buckling resistance test machine.
The result shows that this alloy has high tensile strength and surpasses 4% ductility.The ear shape degree of convexity of the tank body that alloy of the present invention is made is between 0-2.4%, and this quantity on average hangs down 1% than the tank body of being made by 3004 alloys under specified criteria.
The arch counterpressure of the jar of the identical wall thickness that alloy of the present invention is made is much larger than 3004 alloys, and 3004 alloys typically encircle maximum 90 pounds/cun of counterpressure
2, the jar of the identical wall thickness that alloy of the present invention is made is then at 100 and 115 pounds/cun
2Between.
The graphical presentation timeliness of Figure 11 is to the tensile properties and the influence of alloy 2 and 3, and Figure 12 represents that the tensile properties of alloy of the present invention and 3004 types compares.Figure 12 shows that the alloy of the present invention between line A and the B has the tensile strength than the high 20-40% of 3004 type alloys (tradition jar blank), and ductility is high by 4%.So its numerous characteristics is preponderated.
Stronger tank body material means at maintain the standard 3004 the rigidity and the wall thickness of buckling resistance lower tank and can reduce.
As previously mentioned, be suitable for jar alloy of end blank, need minimum back training baking intensity and ductility.
The following treatment step of alloy process of alloy 3 components of embodiment 2:
1) is hot-rolled down to 3.0mm
2) be cold-rolled to 0.8mm from 3.0
3) annealed 1 hour down at 345 ℃
4) sample is divided into two, and one is cold-rolled to 0.43mm, and another is cold-rolled to 0.355mm.
5) two samples carry out 500 ℃, 1 hour solution heat treatment before water quenching.
6) two samples are cold-rolled to 0.315mm then, represent 30% and 10% cold rolling economy respectively.
7) sample is split into 8 samples then, and each sample was through 24 hours natural aging.
8) sample is under 121 ℃, through the artificial aging of 3 hours or 6 hours.
9) half sample baked 20 minutes at 205 ℃ then.
10) each sample carries out tension test and system cup, the results are shown in table 5.
Table 6 shows jar end produce used baking after, the per-cent that intensity and ductility descend.
From the result of embodiment 3 as can be seen, the jar end that bakes manufacturing after having carried out according to the present invention surpasses the minimum needs of intensity and ductility.
Existing AA5182 alloy tank end blank has the yielding stress of 325MPa, the ultimate tensile stress of 370MPa and 8% unit elongation.Can see that a jar end blank that bakes after carrying out according to alloy of the present invention and making method has characteristics than traditional jar end material.
Figure 13 has represented the major advantage that the present invention compares with tradition jar raw alloy, the jar of suitable intensity of the present invention (suitable) with the tradition jar, owing to use the material that approaches, the few consumable material of jar that makes equal amts, thereby the cost that means used alloy material is lower.
Above embodiment shows that the intensity that tank body has, ductility and anisotropy far exceed from the tradition jar resulting characteristic of material alloy.And the jar end material that makes the alloy manufacturing of manufacturing and use according to the present invention have desired characteristic becomes possibility, and split type beverage container jar is by the same alloy manufacturing with alloy component.
Claim partly shows above detailed introduction.
Claims (29)
1, the production method that is used to make aluminium pot base material from a kind of aluminium alloy comprises: the consisting of of this aluminium alloy: the zinc of 3.0-8.0 weight percent, 0.5-3.0 the magnesium of weight percent, iron less than 0.7 weight percent, 0.01-2.0 the silicon of weight percent, 0.05-0.9 the copper of weight percent, 0.1-1.1 the manganese of weight percent, chromium less than 0.3 weight percent, impurity is less than 0.15% of gross weight, aforesaid method comprises the following steps: to melt and is suitable for making described alloyed metal, be cast as and be suitable for rolling shape, be rolled to intermediate gauge in finishing, the above-mentioned alloy material of thermal treatment, cold rolling finally rolling in 2-85% economy scope, this material of tempering heat treatment is to the ductility and the intensity that need.
2,, it is characterized in that having in the above-mentioned aluminium alloy zirconium content in little 0.01 weight percent according to the method for claim 1.
3,, it is characterized in that being dispersed with α-phase in the alloy substrate of its alloy material according to the method for claim 1 and 2.
4,, it is characterized in that its finish to gauge step is economy cold rolling between 10-80% according to the method for claim 1 and 2.
5,, it is characterized in that its finish to gauge step is economy cold rolling between 30-70% according to the method for claim 1 or 2.
6, according to the method for claim 1 or 2, the scope that it is characterized in that its zinc is the 4-6.5 weight percent, magnesium 1.0-2.5 weight percent, manganese 0.3-0.8 weight percent, silicon 0.15-0.3 weight percent, iron height to 0.45 weight percent.Copper 0.10-0.50 weight percent, and chromium height to 0.05 weight percent.
7,, it is characterized in that heat-treating with the homogenizing above-mentioned materials after its casting step according to the method for claim 1.
8,, it is characterized in that after its heat treatment step, carrying out hot-rolled step, subsequent intermediate rolling step according to the method for claim 5.
9, method according to Claim 8 is characterized in that it behind hot-rolled step, and material is hot rolling under sufficiently high temperature, so that coiled material is annealed when rolling state.
10,, it is characterized in that the intermediate rolling step is a cold rolling step according to arbitrary method among the claim 1-8.
11,, it is characterized in that the intermediate rolling step in cold-rolled process comprises comprehensive annealing or intermediary recovery annealing according to the method for claim 7.
12,, it is characterized in that its heat treatment of alloy step is solution heat treatment according to the method for claim 1.
13, a kind of aluminium pot blank of alloy manufacturing has the zinc of 3.0-8.0 weight percent, the magnesium of 0.5-3.0 weight percent, less than the iron of 0.7 weight percent, and the silicon of 0.01-2.0 weight percent, the copper of 0.05-0.9 weight percent.0.1-1.1 the manganese of weight percent, less than the chromium of 0.3 weight percent, impurity is less than 0.15 weight percent of total amount.
14, according to the aluminium pot blank of claim 13, the scope that it is characterized in that zinc content is the 4-6.5 weight percent.
15, according to the aluminium pot blank of claim 13, the scope that it is characterized in that the content of magnesium is the 1.0-2.5 weight percent.
16, according to the aluminium pot blank of claim 13, the scope that it is characterized in that the content of manganese is the 0.3-0.8 weight percent.
17, according to the aluminium pot blank of claim 13, the scope that it is characterized in that silicone content is the 0.15-0.3 weight percent.
18,, it is characterized in that iron level is less than the per-cent of 0.45 weight according to the aluminium pot blank of claim 13.
19, according to the aluminium pot blank of claim 13, the content range that it is characterized in that copper is the 0.10-0.50 weight percent.
20,, it is characterized in that the content range of chromium is less than 0.05 weight percent according to the aluminium pot blank of claim 13.
21,, it is characterized in that there is the zirconium that is less than 0.01 weight percent in this blank, and the content range of zirconium is less than 0.08 weight percent according to the aluminium pot blank of claim 13.
22, according to the aluminium pot blank of claim 13, the content range that it is characterized in that zinc is the 4-6.5 weight percent, magnesium is the 1.0-2.5 weight percent, manganese is the 0.3-0.8 weight percent, silicon 0.15-0.30 weight percent, iron is less than 0.45 weight percent, and copper is the 0.10-0.50 weight percent, chromium is less than 0.05 weight percent, and zirconium is less than 0.01 weight percent.
23, according to arbitrary aluminium pot blank among the claim 13-21, it is characterized in that making alloy material to form melt, cast then and be suitable for rolling shape, this alloy material is rolled to intermediate gauge in carrying out before thermal treatment, material final rolling is cold rolling in economy 2-85% scope, then tempered ductility and the intensity that needs that is heat-treated to of material.
24, according to the aluminium pot blank of claim 23, the economy scope that it is characterized in that finish to gauge is 10-80%.
25, according to the aluminium pot blank of claim 23, the economy scope that it is characterized in that finish to gauge is 30-70%.
26, a kind of split type drinking device comprises a tank body part and can end branch, and described tank body part and can end are divided by jar blank manufacturing arbitrary among the claim 23-25.
27, a kind of split type beverage container comprises a tank body part and can end branch, it is characterized in that, is used for the jar material that tank body part and can end are divided, according to method manufacturing arbitrary among the claim 1-12.
28,, it is characterized in that described vessel is had an appointment and surpass 100 pounds/inch according to the split type beverage container of claim 26
2The arch counterpressure.
29,,, has on average " ear shape " degree of convexity less than 2% through the tank body that deep-drawing is made aluminium pot blank arbitrary among the claim 23-25.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| AUPK189490 | 1990-08-22 | ||
| AUPK1894 | 1990-08-22 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN1060115A true CN1060115A (en) | 1992-04-08 |
Family
ID=3774908
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN91108893A Pending CN1060115A (en) | 1990-08-22 | 1991-08-22 | Be suitable for making the aluminium alloy of jar |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0544758A1 (en) |
| JP (1) | JPH06503854A (en) |
| CN (1) | CN1060115A (en) |
| BR (1) | BR9106787A (en) |
| CA (1) | CA2091355A1 (en) |
| WO (1) | WO1992003586A1 (en) |
| ZA (1) | ZA916651B (en) |
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|---|---|---|---|---|
| CN102994829A (en) * | 2012-09-29 | 2013-03-27 | 吴雅萍 | High-strength aluminium alloy |
| CN103088241A (en) * | 2000-12-21 | 2013-05-08 | 阿尔科公司 | Aluminum alloy products and artificial aging nethod |
| CN103567704A (en) * | 2013-10-28 | 2014-02-12 | 任静儿 | Manufacturing method for aluminum alloy composite material for cooler used for air conditioner |
| CN104903481A (en) * | 2012-12-27 | 2015-09-09 | 株式会社神户制钢所 | Aluminum alloy sheet for DI can body |
| CN105051227A (en) * | 2013-03-29 | 2015-11-11 | 株式会社神户制钢所 | Aluminum alloy sheet for packaging container and method for manufacturing same |
| CN105039878A (en) * | 2014-04-30 | 2015-11-11 | 美铝公司 | Aluminum sheet with enhanced formability and an aluminum container made from aluminum sheet |
| WO2016192040A1 (en) * | 2015-06-02 | 2016-12-08 | GM Global Technology Operations LLC | Aluminum alloy for forming an axisymmetric article |
| CN106544560A (en) * | 2016-10-31 | 2017-03-29 | 宁波市佳利来机械制造有限公司 | A kind of automobile air conditioner compressor housing |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6045632A (en) * | 1995-10-02 | 2000-04-04 | Alcoa, Inc. | Method for making can end and tab stock |
| WO1998018975A1 (en) * | 1996-10-25 | 1998-05-07 | Ole Frederiksen | A method of working hard aluminium of standard type (us) aa 7075 t6 |
| DE69912850T2 (en) | 1998-12-18 | 2004-09-09 | Corus Aluminium Walzprodukte Gmbh | METHOD OF PRODUCING AN ALUMINUM-MAGNESIUM-LITHIUM ALLOY PRODUCT |
| FR2846669B1 (en) | 2002-11-06 | 2005-07-22 | Pechiney Rhenalu | PROCESS FOR THE SIMPLIFIED MANUFACTURE OF LAMINATED PRODUCTS OF A1-Zn-Mg ALLOYS AND PRODUCTS OBTAINED THEREBY |
| DE112004003147B4 (en) | 2003-04-10 | 2022-11-17 | Novelis Koblenz Gmbh | Al-Zn-Mg-Cu alloy |
| US20050238528A1 (en) * | 2004-04-22 | 2005-10-27 | Lin Jen C | Heat treatable Al-Zn-Mg-Cu alloy for aerospace and automotive castings |
| RU2443797C2 (en) * | 2006-07-07 | 2012-02-27 | Алерис Алюминум Кобленц Гмбх | Products from aluminium alloy of aa7000 series and their manufacturing method |
| BR112013005659A2 (en) | 2010-09-08 | 2016-05-03 | Alcoa Inc | improved lithium aluminum alloys, and method for producing the same |
| WO2013172910A2 (en) | 2012-03-07 | 2013-11-21 | Alcoa Inc. | Improved 2xxx aluminum alloys, and methods for producing the same |
| EP2899287B1 (en) * | 2012-09-20 | 2018-03-07 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy plate for automobile part |
| US9587298B2 (en) | 2013-02-19 | 2017-03-07 | Arconic Inc. | Heat treatable aluminum alloys having magnesium and zinc and methods for producing the same |
| TWI601836B (en) * | 2016-06-02 | 2017-10-11 | 中國鋼鐵股份有限公司 | Method for manufacturing aluminum sheet |
| MX2020011510A (en) * | 2018-05-15 | 2020-12-07 | Novelis Inc | High strength 6xxx and 7xxx aluminum alloys and methods of making the same. |
| WO2021067695A1 (en) * | 2019-10-02 | 2021-04-08 | Novelis Inc. | Aluminum flat rolled products with high recycled content for light gauge packaging solutions and related methods |
| JP2021188102A (en) * | 2020-06-02 | 2021-12-13 | 国立大学法人九州大学 | Aluminum alloy material and hydrogen embrittlement inhibitor for aluminum alloy material |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3187428A (en) * | 1960-10-19 | 1965-06-08 | Reynolds Metals Co | Method of treating aluminum and aluminum alloys preparatory to bright finishing |
| CH480883A (en) * | 1964-08-27 | 1969-11-15 | Alusuisse | Process for the production of hardenable strips and sheets from hardenable aluminum alloys with copper contents below 1% |
| DE1483324C2 (en) * | 1965-12-02 | 1975-04-24 | Vereinigte Aluminium-Werke Ag, 5300 Bonn | Use of AIZnMg alloys with low notch sensitivity |
| GB1186161A (en) * | 1966-04-07 | 1970-04-02 | High Duty Alloys Ltd | Improvements in or relating to the Heat Treatment of Aluminium Alloys |
| FR1543955A (en) * | 1967-05-19 | 1968-10-31 | Cegedur | Aluminum alloy road crash barriers |
-
1991
- 1991-08-21 BR BR919106787A patent/BR9106787A/en unknown
- 1991-08-21 CA CA002091355A patent/CA2091355A1/en not_active Abandoned
- 1991-08-21 WO PCT/AU1991/000376 patent/WO1992003586A1/en not_active Application Discontinuation
- 1991-08-21 JP JP3513794A patent/JPH06503854A/en active Pending
- 1991-08-21 EP EP91915278A patent/EP0544758A1/en not_active Withdrawn
- 1991-08-22 CN CN91108893A patent/CN1060115A/en active Pending
- 1991-08-22 ZA ZA916651A patent/ZA916651B/en unknown
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103088241A (en) * | 2000-12-21 | 2013-05-08 | 阿尔科公司 | Aluminum alloy products and artificial aging nethod |
| CN103088241B (en) * | 2000-12-21 | 2015-04-22 | 阿尔科公司 | Aluminum alloy products and artificial aging method |
| CN102994829A (en) * | 2012-09-29 | 2013-03-27 | 吴雅萍 | High-strength aluminium alloy |
| CN104903481A (en) * | 2012-12-27 | 2015-09-09 | 株式会社神户制钢所 | Aluminum alloy sheet for DI can body |
| CN105051227A (en) * | 2013-03-29 | 2015-11-11 | 株式会社神户制钢所 | Aluminum alloy sheet for packaging container and method for manufacturing same |
| CN103567704A (en) * | 2013-10-28 | 2014-02-12 | 任静儿 | Manufacturing method for aluminum alloy composite material for cooler used for air conditioner |
| CN105039878A (en) * | 2014-04-30 | 2015-11-11 | 美铝公司 | Aluminum sheet with enhanced formability and an aluminum container made from aluminum sheet |
| WO2016192040A1 (en) * | 2015-06-02 | 2016-12-08 | GM Global Technology Operations LLC | Aluminum alloy for forming an axisymmetric article |
| US10882104B2 (en) | 2015-06-02 | 2021-01-05 | GM Global Technology Operations LLC | Aluminum alloy for forming an axisymmetric article |
| CN106544560A (en) * | 2016-10-31 | 2017-03-29 | 宁波市佳利来机械制造有限公司 | A kind of automobile air conditioner compressor housing |
| CN106544560B (en) * | 2016-10-31 | 2018-06-05 | 宁波市佳利来机械制造有限公司 | A kind of automobile air conditioner compressor housing |
Also Published As
| Publication number | Publication date |
|---|---|
| ZA916651B (en) | 1992-07-29 |
| CA2091355A1 (en) | 1992-02-23 |
| WO1992003586A1 (en) | 1992-03-05 |
| BR9106787A (en) | 1993-06-29 |
| EP0544758A1 (en) | 1993-06-09 |
| JPH06503854A (en) | 1994-04-28 |
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