EP0851943A1 - Procede de fabrication des feuilles de boites-boisson - Google Patents

Procede de fabrication des feuilles de boites-boisson

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Publication number
EP0851943A1
EP0851943A1 EP96935838A EP96935838A EP0851943A1 EP 0851943 A1 EP0851943 A1 EP 0851943A1 EP 96935838 A EP96935838 A EP 96935838A EP 96935838 A EP96935838 A EP 96935838A EP 0851943 A1 EP0851943 A1 EP 0851943A1
Authority
EP
European Patent Office
Prior art keywords
feedstock
aluminum alloy
weight
quenching
aluminum
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
Application number
EP96935838A
Other languages
German (de)
English (en)
Other versions
EP0851943B1 (fr
Inventor
Tyzh-Chiang Sun
William Betts
Donald G. Harrington
Ian Smith
Edwin J. Westerman
Gavin F. Wyatt-Mair
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Howmet Aerospace Inc
Original Assignee
Alcoa Inc
Kaiser Aluminum and Chemical Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from US08/531,554 external-priority patent/US5772799A/en
Priority claimed from US08/529,644 external-priority patent/US5655593A/en
Priority claimed from US08/529,522 external-priority patent/US6391127B1/en
Priority claimed from US08/538,415 external-priority patent/US5772802A/en
Priority claimed from US08/548,337 external-priority patent/US5769972A/en
Application filed by Alcoa Inc, Kaiser Aluminum and Chemical Corp filed Critical Alcoa Inc
Publication of EP0851943A1 publication Critical patent/EP0851943A1/fr
Application granted granted Critical
Publication of EP0851943B1 publication Critical patent/EP0851943B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0605—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two belts, e.g. Hazelett-process
    • 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
    • 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
    • C22F1/047—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 magnesium as the next major constituent

Definitions

  • the present invention relates to a process for making aluminum alloy beverage containers, and more particularly, to a process for making such can ends and tabs for such containers allowing them to be produced more economically and efficiently.
  • formability is a key characteristic of aluminum alloy to be used in manufacturing cans.
  • Such cans are most frequently produced from aluminum alloys of the 3000 series.
  • Such aluminum alloys contain alloy elements of both magnesium and manganese.
  • the amount of manganese and magne ⁇ sium used in can body stock is generally present at levels less than about 1% by weight.
  • Such lids and tabs are then shipped to the filler of the beverage can and applied once the containers has been filled by a filler.
  • the requirements for can ends and tabs are generally quite different than those for can bodies.
  • alloy AA5182 an aluminum alloy containing relatively high amounts of magne ⁇ sium to provide the added strength necessary for can ends and tabs.
  • AA5182 typically contains magnesium in an amount ranging from 4.4% by weight, thus adding to the cost of the alloy for can ends and tabs.
  • the concepts of the present invention reside in the discovery that aluminum alloys containing lesser amounts of alloying elements can, nonetheless, be used in fabricating can ends and tabs without sacrificing strength by utilizing a fabrication process in which the aluminum alloy, preferably containing less than 2% by weight of magnesium as an alloying element, is formed into sheet stock for making can ends and tabs.
  • the aluminum alloy is strip cast between a pair of continuous moving metal belts to form a hot strip cast feedstock, and then the feedstock is rapidly quenched to prevent substantial pre ⁇ cipitation of aluminum alloying elements as intermetallic compounds.
  • the fabrication pro ⁇ cess can be applied to alloys of the 3000 series such as AA3104 without the need to increase the thickness of the can ends and tabs to achieve comparable strips.
  • the techniques of strip casting followed by rapid quenching provide an alloy sheet stock having improved strength by reason of its eutectic constituents which provide increased strengths.
  • the sequence of steps of strip casting, quenching and rolling is preferably greater within a continuous, in-line sequence. That has a further advantage of eliminating process and material handling steps typically employed in the prior art.
  • the strip casting can be used to produce a cast strip having a thickness less than 1.0 inches, and preferably within the range of 0.01 to 0.2 inches.
  • the widths of the strip is narrow contrary to conventional wisdom. That facilitates ease of in-line threading and processing and allows production lines for the manufacture of can ends and tabs to be physically located with or as part of a can making facility.
  • a filler location that has the further advantage of eliminating addi ⁇ tional handling and shipping costs, thus promoting the overall economics of a can making operation.
  • the aluminum alloy is strip cast between a pair of con ⁇ tinuous moving metal belts to form a hot strip cast feedstock, and then the feedstock is rapidly quenched to prevent substan ⁇ tial precipitation of aluminum alloying elements as intermetallic compounds. Thereafter, with or without addi ⁇ tional rolling, the quenched feedstock is annealed and rapidly quenched, also to prevent substantial precipitation of alloying elements. It has been found that the intermediate annealing and quenching steps substantially improve the formability of the feedstock while maintaining exceptionally high metallurgi ⁇ cal properties including ultimate tensile strength and yield strength.
  • the fabrication pro ⁇ cess can be applied to alloys of the 3000 series such as AA3104 without the need to increase the thickness of the can ends and tabs to achieve comparable strips.
  • the techniques of strip casting followed by rapid quenching provide an alloy sheet stock having improved strength by reason of its solid solution and age hardening.
  • form-ability of the sheet stock of this invention used in forming can ends and tabs is equal to or better than these DC- cast aluminum alloys containing greater quantities of alloying elements.
  • the present invention allows can ends and tabs to be produced from less expensive aluminum alloys without sacrificing the metallurgical properties of those more expen ⁇ sive alloys. It has also been found that the intermediate anneal and quench steps promote the formability of the can end and tab stock without adversely effecting its strength.
  • the aluminum alloy is strip cast, preferably between a pair of continuous moving metal belts, to form a hot strip cast feedstock, and then the feedstock is rapidly, with or without additional rolling, annealed and rapidly quenched to prevent substantial precipitation of alloying elements.
  • the intermediate annealing and quenching steps substantially improve the formability of the feedstock while maintaining exceptionally high metallurgi ⁇ cal properties including ultimate tensile strength and yield strength.
  • the omission of the first quenching step represents more efficient utilization of energy since it is not necessary to reheat the feed stock to the desired annealing temperature after it has been cooled by initial quenching.
  • the omission of such a first quench step as described also makes it more possible to efficiently utilize the concepts of the present invention in a continuous in-line sequence of steps. That, in turn, provides substantial eco ⁇ nomic benefits in carrying out the method of the present inven ⁇ tion. It has been unexpectedly found that such a fabrica ⁇ tion process provides an aluminum alloy feedstock having equal or better metallurgical and formability characteristics as compared to aluminum alloys conventionally used in forming can ends and tabs.
  • the fabrication pro ⁇ cess can be applied to alloys of the 3000 series such as AA3104 without the need to increase the thickness of the can ends and tabs to achieve comparable strengths.
  • the tech ⁇ niques of strip casting followed by rapid annealing and quench ⁇ ing provide an alloy sheet stock having improved strength by reason of solid solution and age hardening.
  • Strip casting followed by a rapid anneal and quench step, either with or without hot rolling before annealing facilitates the rapid processing of the feed stock so that precipitation of alloying elements of intermetallic compounds is substantially minimized.
  • Fig. 1 is a schematic illustration of the continuous in-line sequence of steps employed in the practice of the first embodiment of the invention.
  • Fig. 2 is a schematic illustration of the continuous in-line sequence of steps employed in the practice of the second embodiment of the invention.
  • Fig. 3 is a schematic illustration of the continuous in-line sequence of steps employed in the practice of the third embodiment of the invention.
  • Fig. 4 is a schematic illustration of preferred strip casting apparatus used in the practice of the invention.
  • Fig. 5 is a generalized time-temperature transforma ⁇ tion diagram for aluminum alloys illustrating how rapid heating and quenching serves to eliminate or at least substantially minimize precipitation of alloying elements in the form of intermetallic compounds.
  • Fig. 6 is a schematic illustration showing a process utilizing a continuous in-line sequence of steps for producing aluminum alloy sheet stock.
  • Fig. 7 is a drawing of a blank produced with a convoluted die to control earing in accordance with the inven ⁇ tion.
  • Fig. 8 is a schematic illustration of two continuous sequences of steps employed in accordance with another embodi ⁇ ment of the invention.
  • Fig. 1 The sequence of steps employed in the embodiment of the invention are illustrated in Fig. 1.
  • One of the advances of the present invention is that the processing steps for pro ⁇ ducing sheet stock can be arranged in two continuous in-line sequences whereby the various process steps are carried out in sequence.
  • the practice of the invention in a narrow width make it practical for the present process to be conveniently and economically located in or adjacent to sheet stock customer facilities. In that way, the process of the invention can be operated in accordance with the particular technical and throughput needs for sheet stock users.
  • molten metal is delivered from a furnace not shown in the drawing to a metal degassing and filtering device to reduce dissolved gases and particulate matter from the molten metal, also not shown.
  • the molten metal is immediately converted to a cast feedstock or strip 4 in casting apparatus 3.
  • the feedstock employed in the practice of the present invention can be prepared by any of a number of casting techniques well known to those skilled in the art, including twin belt casters like those described in U.S. Patent No. 3,937,270 and the patents referred to therein. In some appli ⁇ cations, it may be preferable to employ as the technique for casting the aluminum strip the method and apparatus described in co-pending application Serial Nos. 08/184,581, 08/173,663 and 07/173,369, the disclosure of which are incorporated herein by reference.
  • the apparatus includes a pair of endless belts 10 and 12 carried by a pair of upper pulleys 14 and 16 and a pair of corresponding lower pulleys 18 and 20.
  • Each pulley is mounted for rotation, and is a suitable heat resistant pulley.
  • Either or both of the upper pulleys 14 and 16 are driven by suitable motor means or like driving means not illustrated in the drawing for purposes of simplicity.
  • the same is true for the lower pulleys 18 and 20.
  • Each of the belts 10 and 12 is an endless belt and is preferably formed of a metal which has low reactivity with the aluminum being cast. Low-carbon steel or copper are frequently preferred materials for use in the endless belts.
  • the pulleys are positioned, as illustrated in Fig. 2, one above the other with a molding gap therebetween corre ⁇ sponding to the desired thickness of the aluminum strip being cast.
  • Molten metal to be cast is supplied to the molding gap through suitable metal supply means such as a tundish 28.
  • suitable metal supply means such as a tundish 28.
  • the inside of the tundish 28 corresponds substantially in width to the width of the belts 10 and 12 and includes a metal supply delivery casting nozzle 30 to deliver molten metal to the molding gap between the belts 10 and 12.
  • the casting apparatus also includes a pair of cooling means 32 and 34 positioned opposite that position of the endless belt in contact with the metal being cast in the molding gap between the belts.
  • the cooling means 32 and 34 thus serve to cool belts 10 and 12, respectively, before they come into contact with the molten metal.
  • coolers 32 and 34 are posi ⁇ tioned as shown on the return run of belts 10 and 12, respec- tively.
  • the cooling means 32 and 34 can be conventional cooling devices such as fluid nozzles positioned to spray a cooling fluid directly on the inside and/or outside of belts 10 and 12 to cool the belts through their thicknesses. Further details respecting the strip casting apparatus may be found in the cited co-pending applications.
  • the feedstock 4 from the strip caster 3 is moved through optional shear and trim station 5 into optional one or more hot rolling stands 6 where its thick ⁇ ness is decreased.
  • the feedstock is passed to a quenching station 7 wherein the feedstock, still at an elevated temperature from the casting operation, is contacted with a cooling fluid.
  • a cooling fluid Any of a variety of quenching devices may be used in the practice of the invention.
  • the quenching station is one in which a cooling fluid, either in liquid or gaseous form, is sprayed onto the hot feedstock to rapidly reduce its temperature. Suitable cooling fluids include water, air, liquefied gases such as carbon dioxide or nitrogen, and the like. It is important that the quench be carried out quickly to reduce the temperature of the hot feedstock rapidly to prevent substantial precipitation of alloying elements from solid solution.
  • the temperature is reduced from a temperature ranging from about 600 to about 950°F to a tempera ⁇ ture below 550°F, and preferably below 450°F.
  • Fig. 3 of the drawings a generalized graphical representation of the formation of precipitates of alloying elements as a function of time and temperature.
  • Such curves which are generally known in the art as time-temperature transformation or "C" curves, show the formation of coarse and fine particles formed by the precipitation of alloying elements as intermetallic compounds as an aluminum alloy is heated or cooled.
  • the cooling afforded by the quench operation immediately following hot rolling is effected at a rate such that the temperature-time line followed by the aluminum alloy during the quench remains between the ordinate and the curves. That ensures that cooling is effected sufficiently rapidly so as to substantially avoid the precipitation of such alloying elements as intermetallic compounds.
  • the feedstock is passed from the quenching step to one or more cold rolling stands 19 in which the feedstock is worked to harden the alloy and reduce its thickness to finish gauge.
  • the cast strip has an unusually high level of solute supersaturation.
  • the aging step causes the ultimate tensile strength and yield strength to increase along with formability.
  • the cast strip which has been aged can either be coiled until needed or it can be immediately formed into can ends and/or tabs using conventional techniques.
  • the use of the cold rolling step is an optional process step of the present inven ⁇ tion, and can be omitted entirely or it can be carried out in an off-line fashion, depending on the end use of the alloy being processed.
  • carrying out the cold rolling step off-line decreases the economic benefits of the preferred embodiment of the invention in which all of the process steps are carried out in-line.
  • the hot rolling exit temperature is generally maintained within the range of 300 to 1000°F.
  • Hot rolling is typically carried out in temper- atures within the range of 300°F to the solidus temperature of the feedstock.
  • the extent of the reductions in thickness effected by the hot rolling and cold rolling operations of the present invention are subject to a wide variation, depending upon the types of alloys employed, their chemistry and the manner in which they are produced. For that reason, the percentage reduction in thickness of each of the hot rolling and cold rolling opera ⁇ tions of the invention is not critical to the practice of the invention. However, for a specific product, practices for reductions and temperatures must be used. In general, good results are obtained when the hot rolling operation effects reduction in thickness within the range of 15 to 99% and the cold rolling effects a reduction within the range from 10 to 85%.
  • strip casting carried out in accordance with the most preferred embodiment of the invention provides a feedstock which does not necessarily require a hot rolling step as outlined above.
  • the concept of the present invention make it possible to utilize, as sheets stock for fabricating can ends and tabs, aluminum alloys containing smaller quanti ⁇ ties of alloying elements as compared to the prior art.
  • the concepts of the present invention may be applied to aluminum alloys containing less than 2% magne- sium.
  • suitable aluminum alloys include the 3000 series of aluminum alloys such as AA3004 and AA3104. Because of the unique combination of processing steps employed in the practice of the invention, it is possible to obtain strength levels with such low in aluminum content aluminum alloys that are equal to or better than the more expensive aluminum alloy heretofore used.
  • such alloys con ⁇ tain 0 to about 0.6% by weight silicon, from 0 to about 0.8% by weight iron, 0 to about 0.6% by wight copper, about 0.2 to 1.5% by weight manganese, about 0.2 to 2% by weight magnesium and about 0 to about .25% by weight zinc, with the balance being aluminum with its usual impurities.
  • Such aluminum alloys treated in accor ⁇ dance with the practice of the present invention have ultimate tensile strengths and yield strengths greater than 50,000psi.
  • An aluminum alloy with the following composition is strip cast to a thickness of 0.080 inches:
  • the hot cast strip was hot rolled to a thickness of 0.037 inches and then quenched with water. Thereafter, it was cold rolled to a finished gauge of 0.116 inches. The cast strip was then cooled and aged for several hours at 320°F.
  • the ultimate tensile strength (UTS), yield strength (YS) and percent elonga ⁇ tion (%Elg) for the cast strip was determined and is set forth in Table 1.
  • the foregoing aluminum alloy was strip cast to a thickness of 0.080 inches and then subjected to fast air cool quenching. Thereafter, it was hot rolled to a finished gauge of 0.110 inches and stabilized at 320-340°F. Its properties are likewise set forth in Table 1.
  • the aluminum alloy strip cast to a thickness of 0.080 inches and subjected to water quenching. Thereafter, it was cold rolled to a finished gauge of 0.0110 inches and aged at 320-340°F for several hours. Its properties are likewise set forth in Table 1. TABLE_1
  • Example A For purposes of comparison, there is set forth below Examples A & B using, in the case of comparative Example A, conventionally prepared aluminum alloy AA5182 having a finished gauge of 0.0112 inches and, in the case of Example B another, standard can lid aluminum.
  • the compositions and the physical properties associated with them are set forth in the following table. The data shows that it is possible to employ in the practice of the invention, as the aluminum alloy for fabrica ⁇ tion of can lids and tabs, low-aluminum content aluminum alloy without any sacrifice in metallurgic properties.
  • Fig. 2 The second embodiment of the invention utilizing an intermediate anneal step is illustrated in Fig. 2.
  • the strip casting operation in strip caster 3, the optional hot rolling 6 and quench 7 are the same as shown in Fig. 1.
  • the feedstock may be rolled and stored until needed. Alternatively, it may be continuously passed to an optional cold rolling stand 15 and then to a flash annealing furnace 17 in which the feedstock, in either coil or strip form, is rapidly heated. That rapid annealing step provides an improved combination of metallic properties such as grain size, strength and formability. Because the feedstock is rapidly heated, substantial precipitation of alloying elements is likewise avoided. Thus the heating operations should be carried out to the desired annealing and recrystallization temperature such that the temperature-time line followed by the aluminum alloy does not cross the C-curves illustrated in Fig. 5 in such a way as to cause substantial precipitation.
  • a quench station 18 Immediately following the heater 17 is a quench station 18 in which the strip is rapidly cooled or quenched by means of a conventional cooling fluid to a temperature suitable for cold rolling. Because the feedstock is rapidly cooled in the quench step 18, there is insufficient time to cause any substantial precipitation of alloying elements from solid solution.
  • the feedstock is passed from the quenching step to one or more cold -23-
  • the feedstock is worked to harden the alloy and reduce its thickness to finish gauge.
  • the strip which has been aged can either be coiled until needed or it can be immediately formed into can ends and/or tabs using conventional techniques.
  • the use of the cold rolling step is an optional process step of the present inven ⁇ tion, and can be omitted entirely or it can be carried out in an off-line fashion, depending on the end use of the alloy being processed.
  • carrying out the cold rolling step off-line decreases the economic benefits of the preferred embodiment of the invention in which all of the process steps are carried out in-line.
  • the hot rolling exit temperature is generally maintained within the range of 300 to 1000°F.
  • Hot rolling is typically carried out in temper ⁇ atures within the range of 300°F to the solidus temperature of the feedstock.
  • the annealing step in which the feedstock is sub ⁇ jected to solution heat treatment to cause recrystallization is effected at a temperature within the range of 600 to 1200°F for less than 120 seconds, and preferably 0.1 to 10 seconds.
  • the feedstock in the form of strip 4 is water quenched to temperatures necessary to continue to retain alloying elements in solid solution, typi ⁇ cally at temperatures less than 400°F.
  • the extent of the reductions in thickness effected by the hot rolling and cold rolling operations of the present invention are subject to a wide variation, depending upon the types of alloys employed, their chemistry and the manner in which they are produced. For that reason, the percentage reduction in thickness of each of the hot rolling and cold rolling opera ⁇ tions of the invention is not critical to the practice of the invention. In general, good results are obtained when the hot rolling operation effects reduction in thickness within the range of 15 to 99% and the cold rolling effects a reduction within the range from 10 to 85%.
  • strip casting carried out in accor ⁇ dance with the most preferred embodiment of the invention provides a feedstock which does not necessarily require a hot rolling step as outlined above.
  • this embodiment of the present inven ⁇ tion make it possible to utilize, as sheets stock for fabricat ⁇ ing can ends and tabs, aluminum alloys containing smaller quantities of alloying elements as compared to the prior art.
  • the concepts of the present invention may be applied to aluminum alloys containing less than 2% magnesium.
  • Represen-tative of suitable aluminum alloys include the 3000 series of aluminum alloys such as AA3004 and AA3104. Because of the unique combination of processing steps employed in the practice of the invention, it is possible to obtain strength and formability levels with such low alloy content aluminum alloys that are equal to or better than the more expensive aluminum alloy heretofore used.
  • such alloys contain 0 to about 0.6% by weight silicon, from 0 to about 0.8% by weight iron, 0 to about 0.6% by weight copper, about 0.2 to 1.5% by weight manganese, about 0.2 to 2% by weight magnesium and about 0 to about .25% by weight zinc, with the balance being aluminum with its usual impurities.
  • the hot cast strip was then immediately rolled to a thickness of 0.045 inches and heated for five seconds at a temperature of 1000°F and immediately thereafter quenched in water.
  • the feedstock was then rolled to a thickness of 0.0116 inches and stabilized at 320°F for two hours at finish gauge. It had an ultimate tensile strength of 56,000 psi, a yield strength of 50,600 psi and 7.2% elongation.
  • the third embodiment of the invention is shown in Fig. 3 of the drawings and utilizes an annealing step prior to quenching.
  • the strip casting operation 3 and the optional hot rolling 6 operations are the same as described in relation to Figs. 1 and 2.
  • the feedstock is passed to a annealing furnace 7 wherein the feedstock, still at an elevated temperature from the casting operation, is rapidly heated, as by flash annealing. That rapid annealing provides an improved combination of metallurgical properties such as grain size, strength and formability. Because the feed stock is rapidly heated, substantial precipitation of alloying elements is avoided.
  • a quench station 8 Immediately following the heater 7 is a quench station 8 in which the feed stock is rapidly cooled or quenched by means of a conventional cooling fluid to a temperature suitable for cold rolling. Because the feed stock is rapidly cooled in the quench station 8, there is likewise insufficient time to cause any substantial precipitation of alloying ele ⁇ ments from solid solution. It is important as before that the quench be carried out quickly to reduce the temperature of the hot feed stock rapidly to prevent substantial precipitation of alloying elements from solid solution.
  • Fig. 3 of the drawings a generalized graphical representation of the formation of precipitates of alloying elements as a function of time and temperature.
  • the heating effected in the annealing step and the cooling effected by the quench operation immediately following annealing is effected at a rate such that the temperature-time line followed by the aluminum alloy during the heating and quenching remains between the ordinate and the curves. That ensures that heating and cooling is effected sufficiently rapidly so as to avoid substantial precipitation of such alloying elements as intermetallic compounds.
  • the feedstock is passed from the quenching step to one or more cold rolling stands 19 in which the feedstock is worked to harden the alloy and reduce its thickness to finish gauge.
  • cold rolling it is sometimes desirable, after cold rolling to age the cold-rolled strip at an elevated temperature, preferably at temperatures within the range of 220-400°F for about 1 to about 10 hours. Because the strip has been quenched immediately following annealing so as to substantially minimize precipita ⁇ tion of alloying elements as intermetallic compounds, the cast strip has an unusually high level of solute supersaturation.
  • the aging step causes the ultimate tensile strength and yield strength to increase along with formability.
  • the strip which has been aged can either be coiled until needed or it can be immediately formed into can ends and/or tabs using conventional techniques.
  • the use of the cold rolling step is an optional process step of the present invention, and can be omitted entirely or it can be carried out in an off-line fashion, depending on the end use of the alloy being processed.
  • carrying out the cold rolling step off-line decreases the economic benefits of the preferred embodiment of the invention in which all of the process steps are carried out in-line.
  • the hot rolling exit temperature is generally maintained within the range of 300 to 1000°F.
  • Hot rolling is typically carried out in temper ⁇ atures within the range of 300°F to the solidus temperature of the feedstock.
  • the annealing step in which the feedstock is sub ⁇ jected to solution heat treatment to cause recrystallization is effected at a temperature within the range of 600 to 1200°F for less than 120 seconds, and preferably 0.1 to 10 seconds.
  • the feedstock in the form of strip 4 is quenched to temperatures necessary to continue to retain alloying elements in solid solution, typically at tem ⁇ peratures less than 550°F.
  • the extent of the reductions in thickness effected by the hot rolling and cold rolling operations of this embodiment of the invention are subject to a wide variation, depending upon the types of alloys employed, their chemistry and the manner in which they are produced. For that reason, the percentage reduction in thickness of each of the hot rolling and cold rolling operations of the invention is not critical to the practice of the invention. In general, good results are ob ⁇ tained when the hot rolling operation effects reduction in thickness within the range of 15 to 99% and the cold rolling effects a reduction within the range from 10 to 85%.
  • strip casting carried out in accordance with the most preferred embodiment of the invention provides a feedstock which does not necessarily require a hot rolling step as outlined above.
  • the concept of the present invention make it possible to utilize, as sheets stock for fabricating can ends and tabs, aluminum alloys containing smaller quanti ⁇ ties of alloying elements as compared to the prior art.
  • the concepts of the present invention may be applied to aluminum alloys containing less than 2% magne- siu .
  • suitable aluminum alloys include the 3000 series of aluminum alloys such as AA3004 and AA3104. Because of the unique combination of processing steps employed in the practice of the invention, it is possible to obtain strength and formability levels with such low alloy content aluminum alloys that are equal to or better than the more expensive aluminum alloy heretofore used.
  • such alloys contain 0 to about 0.6% by weight silicon, from 0 to about 0.8% by weight iron, 0 to about 0.6% by weight copper, about 0.2 to 1.5% by weight manganese, about 0.2 to 2% by weight magnesium and about 0 to about .25% by weight zinc, with the balance being aluminum with its usual impurities.
  • the hot cast strip was then immediately rolled to a thickness of 0.045 inches and heated for five seconds at a temperature of 1000°F and immediately thereafter quenched in water.
  • the feedstock was then rolled to a thickness of 0.0116 inches and stabilized at 320°F for two hours at finish gauge. It had an ultimate tensile strength of 56,000 psi, a yield strength of 50,600 psi and 7.2% elongation.
  • the continuous annealing furnace preferably used in the practice of the process dis ⁇ closed in the foregoing application must be made longer and be run at higher energy levels, representing an increase in the cost of capital equipment and the cost in operating the pro ⁇ cess. It would, therefore, be desirable that the continuous annealing step be avoided.
  • aluminum alloy sheet stock and preferably aluminum alloy can body stock having desirable metallurgical properties by using, in one continuous sequence of steps, the steps of providing a hot aluminum alloy feedstock which is subjected to a series of rolling steps to rapidly and continuously cool the feedstock to the thickness and metallurgical properties without the need to employ an annealing step conventionally used in the prior art.
  • simi ⁇ lar prior art processes such as that described in U.S. Patent No. 4,282,04444
  • aluminum alloy can body stock can be produced by strip casting, followed by roll ⁇ ing and coiling whereby the rolled feedstock in the form of coils is allowed to slowly cool. Thereafter, the coil is later annealed to improve the metallurgical properties of the sheet stock.
  • the feedstock produced by the method of the present invention is characterized as being produced in a highly economical fashion without the need to employ a costly anneal ⁇ ing step.
  • annealing has been used in the prior art to minimize earing. It has been found, in accordance with the practice of this invention, that, the conditions (time and temperature) of hot rolling, the thickness of the alloy as strip cast and the speed at which it is cast can be used to control earing. For exam ⁇ ple, casting the aluminum alloy at reduced thickness is be ⁇ lieved to reduce earing; similarly, casting at higher speeds can likewise reduce earing. Nonetheless, where use is made of processing conditions which tend to yield an aluminum alloy strip having a tendency toward higher earing, that phenomenon can be controlled by means of an alternative embodiment.
  • the high earing that can occur on the feedstock can be compensated for by cutting the processed feedstock into non-circular blanks prior to cupping, using what has become known in the art as convoluted die.
  • the use of a convoluted die compensates for any earing tendencies of the sheet stock, by removing metal from those peripheral portions of the blank which would be converted to ears on cup-drawing.
  • the convoluted die offsets any earing that would otherwise be caused by the omission of high temperature annealing.
  • the strip is fabricated by strip casting to produce a cast thickness less than 1.0 inches, and preferably within the range of 0.01 to 0.2 inches.
  • the width of the strip, slab or plate is narrow, contrary to conventional wis ⁇ dom; this facilitates ease of in-line threading and processing, minimizes investment in equipment and minimizes cost in the conversion of molten metal to can body stock.
  • the preferred process of the present invention involves a new method for the manufacture of aluminum alloy cups and can bodies utilizing the following process steps in one, continuous in-line sequence:
  • a hot aluminum feedstock is provided, preferably by strip casting; and
  • the feedstock is, in the preferred embodiment, subjected to rolling to rapidly and continu ⁇ ously cool the sheet stock to the desired thickness and attain the desired strength prop ⁇ erties.
  • the cooled feedstock can then be either formed into a coil for later use or can be further processed to form non-circular blanks by means of a convoluted die to effect earing control, in accordance with conventional procedures.
  • the rolling of the freshly cast strip be ef ⁇ fected rapidly, before there is sufficient time for the diffusion-controlled reaction by which alloying elements are precipitated from solid solution as intermetallic compounds.
  • the process of the present invention makes it possible to omit high temperature annealing as is required in the prior art to effect solution of soluble alloying elements.
  • the cast feedstock must be cooled to cold rolling temperatures in less than 30 second, and preferably in less than 10 seconds.
  • the overall process of the present invention embodies characteristics which differ from the prior art processes: ⁇ -S ⁇ -
  • the can body stock is produced by utilizing small, in-line, simple machinery
  • the in-line arrangement of the processing steps in a narrow width makes it possible for the process to be conveniently and economically located in or adja ⁇ cent to can production facilities. In that way, the process of the invention can be operated in accordance with the particular technical and throughput needs for can stock of can making facilities.
  • molten metal is delivered from a furnace 1 to a metal degassing and filtering device 2 to reduce dissolved gases and particulate matter from the molten metal, as shown in Fig. 1
  • the molten metal is immediately converted to a cast feedstock 4 in casting appara ⁇ tus 3.
  • feedstock refers to any of a variety of aluminum alloys in the form of ingots, plates, slabs and strips delivered to the hot rolling step at the required temperatures.
  • an aluminum "ingot" typically has a thickness ranging from about 6 inches to about 30 inches, and is usually produced by direct chill casting or electromagnetic casting.
  • An aluminum “plate”, on the other hand, herein refers to an aluminum alloy having a thickness from about 0.5 inches to about 6 inches, and is typically produced by direct chill casting or electromagnetic casting alone or in combination with hot rolling of an aluminum alloy.
  • the term “slab” is used herein to refer to an aluminum alloy having a thickness ranging from 0.375 inches to about 3 inches, and thus overlaps with an aluminum plate.
  • the term “strip” is herein used to refer to an aluminum alloy, typically having a thickness less than 0.375 inches. In the usual case, both slabs and strips are produced by continuous casting techniques well known to those skilled in the art.
  • the feedstock employed in the practice of this embodiment of the present invention can be prepared by any of a number of casting techniques well known to those skilled in the art, including twin belt casters like those described in U.S. Patent No. 3,937,270 and the patents referred to therein.
  • it is preferable to employ as the technique for casting the aluminum strip the method and apparatus de ⁇ scribed in co-pending Application Serial Nos. 184,581, filed June 21, 1994, 173,663, filed December 23, 1993 and 173,369, filed December 23, 1990, the disclosures of which is incorpo ⁇ rated herein by reference.
  • the strip casting technique de ⁇ scribed in the foregoing co-pending applications which can advantageously be employed in the practice of this invention is illustrated in Fig. 4 of the drawing as described above.
  • the feedstock 4 is moved through optional pinch rolls 5 into one or more hot rolling stands 6 where its thick ⁇ ness is decreased.
  • the rolling stands serve to rapidly cool the feedstock to prevent or inhibit precipitation of the strengthening alloying components such as manganese, copper, magnesium and silicon present in the aluminum alloy.
  • the exit temperature from the strip caster 3 varies within the range of about 700°F to the solidus temperature of the alloy.
  • the rolling operations rapidly cool the temperature of the cast strip 4 to temperatures suitable for cold rolling, generally below 350°F in less than 30 seconds, and preferably in less than 10 seconds, to ensure that the cooling is effected suffi ⁇ ciently rapidly to avoid or substantially minimize precipita ⁇ tion of alloying elements from solid solution.
  • the effect of the rapidly cooling may be illustrated by reference to Fig. 5 of the drawing, showing the formation of intermetallic precipi ⁇ tates in aluminum as a function of temperature and time.
  • the effect of the reductions in thickness likewise effected by the rolling operations are subject to wide varia ⁇ tion, depending upon the types of feedstock employed, their chemistry and the manner in which they are produced. For that reason, the percent reduction in thickness of the rolling operations is not critical to the practice of the invention. In general, good results are obtained when the rolling opera ⁇ tion effects a reduction in thickness within the range of 40 to 99 percent of the original thickness of the cast strip.
  • Convo ⁇ luted dies useful in the practice of the present invention are known to the art, and are described in U.S. Patent Nos. 4,711,611 and 5,095,733. Such dies are now conventional and well known to those skilled in the art.
  • the convoluted dies used in the practice of this invention may be used to form a non-circular blank having the configuration shown in Fig. 7 which in turn can be used to form a cup having the configura ⁇ tion shown in the same Figure.
  • the convoluted die can be used, where necessary, to minimize earing tendencies of the sheet stock.
  • alloys suitable for use in the practice of the present invention are those aluminum alloys containing from about 0 to about 0.6% by weight silicon, from 0 to about 0.8% by weight iron, from about 0 to about 0.6% by weight copper, from about 0.2 to about 1.5% by weight manga ⁇ nese, from about 0.2 to about 4% by weight magnesium, from about 0 to about 0.25% by weight zinc, with the balance being aluminum with its usual impurities.
  • suitable alloys include aluminum alloys from the 3000 and 5000 series, such as AA 3004, AA 3104 and AA 5017.
  • a sheet of finish gauge can stock which was not annealed was formed into a cup using a conventional round die. The earing was measured as 6.6%.
  • An adjacent sheet from the same processing (still without an anneal) was formed into a cup with a convolute cut edge on the blanking die.
  • the earing was measured as 3.1%.
  • a thin strip of metal 0.09 inch thick was cast at 300 feet per minute and immediately rolled in three passes at high speed from 0.090 inch thick to 0.0114 inch thick while decreasing in temperature during rolling from 900°F to 300°F.
  • the earing of the sheet so produced was 3.8%.
  • the ultimate tensile strength of the sheet was 43,400 psi and the elongation 4.4%.
  • a variation of the continuous in-line operation for aluminum alloy can stock disclosed and claimed in United States Patent No. 5,356,495 in which use is made of two sequences of continuous, in-line operations.
  • the aluminum alloy feedstock is first subjected to hot rolling, coiling and coil self annealing and the second sequence in ⁇ cludes the continuous, in-line sequence of uncoiling, quenching without intermediate cooling, cold rolling and coiling.
  • the process as described in the latter patent has the advantage of eliminating the capital costs of an annealing furnace while nonetheless providing aluminum sheet and can stock having strength associated with aluminum alloys which have been heat treated.
  • the first sequence includes a quenching step and the second sequence includes a rapid annealing step to provide aluminum alloy sheet stock and can stock having highly desirable metallurgical properties. It has been found that the rapid quenching in the first sequence of steps and the rapid heating followed by quenching in the second sequence of steps do not permit substantial precipita ⁇ tion of alloying elements present in the alloy and, thus, affords an aluminum alloy sheet and can stock having highly desirable metallurgical properties.
  • the aluminum alloy sheet can be flash annealed and rapidly quenched to ensure that alloying elements are in solid solution.
  • the annealing followed by quenching in the second sequence of steps maximizes alloying elements in solid solution to strengthen the final product.
  • anneal or “flash anneal” refers to a heating process to effect recrystallization of the grains of aluminum alloy to produce uniform formability and to control earing. Flash annealing, as referred to herein, refers to a rapid annealing process which serves to recrystallize the aluminum grains without causing substantial precipitation of intermetallic compounds. Slow heating and cooling of the aluminum alloy are known to cause substantial precipitation of intermetallic compounds. Therefore, it is an important concept of the invention that the heating, flash annealing and quench- ing be carried out rapidly. The continuous operation in place of batch processing facilitates precise control of process conditions and therefore metallurgical properties. Moreover, carrying out the process steps continuously and in-line elimi ⁇ nates costly materials handling steps, in-process inventory and losses associated with starting and stopping the processes.
  • the process of the present invention thus involves a new method for the manufacture of aluminum alloy sheet and can body stock utilizing the following process steps in two con ⁇ tinuous, in-line sequences.
  • the follow ⁇ ing steps are carried out continuously and in-line:
  • the quenched feedstock is, in the preferred em ⁇ bodiment of the invention, subjected to cold rolling to produce intermediate gauge sheet ;
  • the feedstock is uncoiled and, optionally, can be subjected to cold rolling if desired to further reduce the thickness of the stock;
  • the flash anneal and the quench operation be carried out rapidly to ensure that alloying elements, and particularly manganese, as well as compounds of copper, silicon, magnesium and aluminum, remain in solid solution.
  • alloying elements and particularly manganese, as well as compounds of copper, silicon, magnesium and aluminum, remain in solid solution.
  • the precipitation hardening of aluminum is a diffusion de ⁇
  • the flash annealing and quenching operations of the second sequence of steps be carried out sufficiently rap ⁇ idly that there is insufficient time to result in substantial precipitation of intermetallic compounds of copper, silicon, magnesium, iron, aluminum and manganese.
  • the annealing and quenching operations of the second step likewise minimize earing. That is particularly important when the aluminum alloy is a can stock alloy since earing is a phenome ⁇ non frequently found in the formation of cans from can body stock in which the plastic deformation to which the aluminum alloy is subjected is non-uniform.
  • minimizing precipita ⁇ tion of intermetallic compounds raises the strength, allows recrystallization to be done at a lighter gauge, minimizes finish cold work and thereby reduces earing.
  • the strip is fabricated by strip casting to produce a cast thickness less than 1.0 inches, and preferably within the range of 0.06 to 0.2 inches.
  • the width of the strip, slab or plate is narrow, contrary to conventional wisdom. This facilitates ease of in-line threading and processing, minimizes investment in equipment and minimizes cost in the conversion of molten metal to the sheet stock.
  • the sequence of steps employed in this embodiment of the invention are illustrated in Fig. 8.
  • One of the advances of the present invention is that the processing steps for pro ⁇ ducing sheet stock can be arranged in two continuous in-line sequences whereby the various process steps are carried out in sequence.
  • molten metal is delivered from a furnace not shown in the drawing to a metal degassing and filtering device to reduce dissolved gases and particulate matter from the molten metal, also not shown.
  • the molten metal is immediately converted to a cast feedstock 4 in casting apparatus 3.
  • the feedstock is passed to a quenching station 7 wherein the feedstock, still at an elevated temperature from the casting operation, is con ⁇ tacted with a cooling fluid.
  • a quenching station 7 Any of a variety of quenching devices may be used in the practice of the invention.
  • the quenching station is one in which a cooling fluid, either in liquid or gaseous form, is sprayed onto the hot feedstock to rapidly reduce its temperature.
  • Suitable cooling fluids include water, liquified gases such as carbon dioxide or nitrogen, and the like. It is important that the quench be carried out quickly to reduce the temperature of the hot feedstock rapidly to prevent substantial precipitation of alloying elements from solid solution.
  • the temperature is reduced from a temperature ranging from about 600 to about 950°F to a tempera ⁇ ture below 550°F, and preferably below 450°F.
  • the feedstock can be coiled using conventional coiling apparatus in a coiler 8.
  • the feedstock 4 can be subjected to cold rolling as an optional step prior to cooling.
  • Fig. 5 of the drawings a generalized graphical representation of the formation of precipitates of alloying elements as a function of time and temperature.
  • Such curves which are generally known in the art as time/temperature-transformation or "C" curves, show the forma ⁇ tion of coarse and fine particles formed by the precipitation of alloying elements as intermetallic compounds as an aluminum alloy is heated or cooled.
  • C time/temperature-transformation
  • the cooled feedstock can be stored until needed.
  • the temperature of the feedstock has been previ ⁇ ously rapidly reduced in the quenching station 7 to prevent substantial precipitation of alloying elements and compounds thereof; hence the coil can be stored indefinitely.
  • the stored coil can then be subjected to the second continuous, in-line sequence of steps, also as shown in Fig. 8.
  • the coil previously formed is placed in an uncoiler 13 from which it is passed to an optional cold rolling station 15 and then to a flash annealing furnace 17 in which the coil is rapidly heated. That rapid annealing step provides an improved combination of metallurgical properties such as grain size, strength and formability.
  • the heating operation should be carried out to the desired annealing or recrystallization temperature such that the temperature-time line followed by the aluminum alloy does not cross the C-curves illustrated in Fig. 5 in such a way as to cause substantial precipitation.
  • a quench station 15 Immediately following the heater 14 is a quench station 15 in which the strip is rapidly cooled by means of a conventional cooling fluid to a temperature suitable for cold rolling. Because the feedstock is rapidly cooled in the quench step 15, there is insufficient time to cause any substantial precipitation of alloying elements from solid solution. That facilitates higher than conventional strength. This reduces the amount of strengthening required by cold working, and less cold working reduces earing.
  • the feedstock is passed from the quenching step to one or more cold rolling stands 19 in which the feedstock is worked to harden the alloy and reduce its thickness to finish gauge. After cold rolling, the strip 4 is coiled to a coiler 21.
  • the use of the cold rolling step is an optional process step of the present invention, and can be omitted entirely or it can be carried out in an off-line fashion, depending on the end use of the alloy being processed.
  • carrying out the cold rolling step off-line decreases the economic benefits of the preferred embodiment of the invention in which all of the process steps are carried out in-line.
  • the hot rolling exit temperature is generally maintained within the range of 300 to 1000°F.
  • Hot rolling is typically carried out in temper- atures within the range of 300°F to the solidus temperature of the feedstock.
  • the annealing and solution heat treatment is effected at a temperature within the range of 600 to 1200°F for less than 120 seconds, and preferably 0.1 to 10 seconds.
  • the feedstock in the form of strip 4 is water quenched to tempera ⁇ tures necessary to continue to retain alloying elements in solid solution and to cold roll (typically less than 400°F) .
  • the extent of the reductions in thickness effected by the hot rolling and cold rolling operations of the present invention are subject to a wide variation, depending upon the types of alloys employed, their chemistry and the manner in which they are produced. For that reason, the percentage reduction in thickness of each of the hot rolling and cold rolling opera ⁇ tions of the invention is not critical to the practice of the invention. However, for a specific product, practices for reductions and temperatures must be used. In general, good results are obtained when the hot rolling operation effects reduction in thickness within the range of 15 to 99% and the cold rolling effects a reduction within the range from 10 to 85%.
  • strip casting carried out in accordance with the most preferred embodiment of the invention provides a feedstock which does not necessarily require a hot rolling step as outlined above.
  • the hot rolling step can be avoided alto ⁇ gether and, thus, is optional in the practice of the invention.
  • alloys from the 1000, 2000, 3000, 4000, 5000, 6000, 7000 and 8000 series are suitable for use in the practice of the present invention.
  • sample feedstock was as cast aluminum alloy solidified rapidly enough to have secondary dendrite arm spac ⁇ ings below 10 microns.
  • an aluminum alloy having the composition set forth in Table 3 and a prior art example are each carried out by casting aluminum alloys using a twin belt strip caster in which the belts are cooled while they are not in contact with either molten metal or the cast metal strip to yield a cast metal strip having a thickness of 0.10 inches.
  • the cast stip is then processed as indicated in the Table for each of the examples to yield the products whose characteris ⁇ tics are set forth in Table 3.
  • the prior art process illus ⁇ trated is that in U.S. Patent No. 4,292,044, except that the strip casting in the prior art process is carried out using the same technique as Tests 1 and 2.
  • Table 3 also sets forth typical data for aluminum alloys having the composition set forth therein for AA3104 and AA5182 produced by the conven ⁇ tional ingot process in which the ingots have thicknesses of 26 inches. Can buckle strengths are set forth for all alloys except 5182, and have been corrected to 0.0112 inch gauge for ease of comparison.
  • the Tests illustrate the unexpected results produced by the present invention. Rapid quenching instead of slow cooling in accordance with the concepts of this invention results in significantly higher strength, either with or with ⁇ out hot rolling.
  • the strengths obtained in the practice of this invention for low alloy content aluminum alloys approaches that of AA5182, a high alloy content aluminum alloy typically used for can lids and tabs, as the data shows. Not only does the process of the invention provide superior strength, it provides equivalent or lower earing as well.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Continuous Casting (AREA)
  • Metal Rolling (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Abstract

L'invention concerne un procédé amélioré de fabrication de boîtes-boisson en alliages d'aluminium, y compris les extrémités et les languettes, ledit procédé consistant à soumettre les alliages en question aux opérations suivantes: coulage de bandes puis une ou plusieurs séries d'étapes de refroidissement et de recuit. On décrit par ailleurs la production de charge d'alimentation pour boîtes-boisson en alliages d'aluminium par une opération de laminage à chaud qui suit immédiatement le coulage de bandes afin de réduire l'épaisseur de cette charge, qu'elle soit soumise ou non à un bobinage intermédiaire.
EP96935838A 1995-09-18 1996-09-17 Procede de fabrication des feuilles de boites-boisson Expired - Lifetime EP0851943B1 (fr)

Applications Claiming Priority (11)

Application Number Priority Date Filing Date Title
US548337 1983-11-03
US08/531,554 US5772799A (en) 1995-09-18 1995-09-18 Method for making can end and tab stock
US08/529,644 US5655593A (en) 1995-09-18 1995-09-18 Method of manufacturing aluminum alloy sheet
US529644 1995-09-18
US529522 1995-09-18
US531554 1995-09-18
US08/529,522 US6391127B1 (en) 1992-06-23 1995-09-18 Method of manufacturing aluminum alloy sheet
US538415 1995-10-02
US08/538,415 US5772802A (en) 1995-10-02 1995-10-02 Method for making can end and tab stock
US08/548,337 US5769972A (en) 1995-11-01 1995-11-01 Method for making can end and tab stock
PCT/US1996/014877 WO1997011205A1 (fr) 1995-09-18 1996-09-17 Procede de fabrication des feuilles de boites-boisson

Publications (2)

Publication Number Publication Date
EP0851943A1 true EP0851943A1 (fr) 1998-07-08
EP0851943B1 EP0851943B1 (fr) 2003-05-21

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JP (1) JP3878214B2 (fr)
CN (1) CN1085743C (fr)
AU (1) AU722391B2 (fr)
BR (1) BR9611416A (fr)
CA (1) CA2232436C (fr)
DE (1) DE69628312T2 (fr)
ES (1) ES2196183T3 (fr)
WO (1) WO1997011205A1 (fr)

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CN106424325B (zh) * 2015-08-06 2019-07-26 珠海鼎立包装制品有限公司 一种加强型拉环的生产工艺及专用设备
TWI601836B (zh) * 2016-06-02 2017-10-11 中國鋼鐵股份有限公司 鋁片之製造方法
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ES2905306T3 (es) 2016-10-27 2022-04-07 Novelis Inc Aleaciones de aluminio serie 7xxx de alta resistencia y procedimientos para fabricar las mismas
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CN106756673A (zh) * 2016-12-20 2017-05-31 上海赛科利汽车模具技术应用有限公司 一种7075铝合金材料的汽车b柱加工工艺
JP6427290B1 (ja) * 2017-11-22 2018-11-21 株式会社Uacj 磁気ディスク用アルミニウム合金基板及びその製造方法、ならびに、当該磁気ディスク用アルミニウム合金基板を用いた磁気ディスク
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WO2021067695A1 (fr) * 2019-10-02 2021-04-08 Novelis Inc. Produits laminés à plat d'aluminium à haute teneur en matériaux recyclés pour solutions de conditionnement à faible épaisseur et procédés associés

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AU722391B2 (en) 2000-08-03
ES2196183T3 (es) 2003-12-16
CN1200771A (zh) 1998-12-02
CA2232436C (fr) 2008-06-17
JP3878214B2 (ja) 2007-02-07
BR9611416A (pt) 1999-02-23
JPH11511389A (ja) 1999-10-05
EP0851943B1 (fr) 2003-05-21
CN1085743C (zh) 2002-05-29
AU7362596A (en) 1997-04-09
CA2232436A1 (fr) 1997-03-27
DE69628312T2 (de) 2004-03-25
MX9802071A (es) 1998-08-30
DE69628312D1 (de) 2003-06-26
WO1997011205A1 (fr) 1997-03-27

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