EP2698216A1 - Procédé de fabrication d'un alliage d'aluminium destiné à être utilisé dans la construction automobile - Google Patents

Procédé de fabrication d'un alliage d'aluminium destiné à être utilisé dans la construction automobile Download PDF

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Publication number
EP2698216A1
EP2698216A1 EP13178860.6A EP13178860A EP2698216A1 EP 2698216 A1 EP2698216 A1 EP 2698216A1 EP 13178860 A EP13178860 A EP 13178860A EP 2698216 A1 EP2698216 A1 EP 2698216A1
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Prior art keywords
strip
aluminum alloy
annealing
hot
line
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EP13178860.6A
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German (de)
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EP2698216B1 (fr
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David A. Tomes, Jr
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Arconic Technologies LLC
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Alcoa Inc
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    • 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
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/003—Aluminium alloys
    • 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
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • 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 disclosure relates to uses of continuously cast aluminum-magnesium alloy sheets components in automotive manufacturing.
  • the sheet is annealed to an O-temper and has a yield point elongation less than 0.6%.
  • the present disclosure also relates to methods for manufacturing an aluminum alloy in a continuous in-line sequence wherein the aluminum alloy is adapted and intended to be used in the manufacturing of an automobile.
  • the present disclosure also relates to the use of an aluminum alloy manufactured with such a method for components in automotive manufacturing.
  • U.S. Patent No. 7,182,825 discloses a method of making aluminum alloy sheets in a continuous in-line process. The entire contents of U.S. Patent No. 7,182,825 is incorporated herein in full.
  • a continuously-cast aluminum alloy strip is optionally quenched, hot or warm rolled, annealed or heat-treated in-line, optionally quenched, and preferably coiled, with additional hot, warm, or cold rolling steps as needed to reach the desired gauge.
  • the process can be used to make aluminum alloy sheet of T or O temper.
  • U.S. Patent No. 6,672,368 discloses a method of continuously-casting aluminum alloy strips. The entire contents of U.S. Patent No. 6,672,368 is incorporated herein in full.
  • the method includes continuous casting aluminum alloys between a pair of rolls. Molten aluminum alloy is delivered to a roll bite between the rolls and passes into the roll nip - or point of minimum clearance of between the rolls - in a semi-molten state. A solid strip of cast aluminum alloy exits the nip at speed ranging from 25 to 400 feet per minute; alternatively from 50 feet per minute to 350 feet per minute.
  • U.S. Patent No. 5,655,593 describes a method of making aluminum alloy sheet where a thin strip is cast (in place of a thick ingot) which is rapidly rolled and continuously cooled for a period of less than 30 seconds to a temperature of less than 350°F.
  • U.S. Patent No. 5,772,802 describes a method in which the aluminum alloy cast strip is quenched, rolled, annealed at temperatures between 600° and 1200°F for less than 120 seconds, followed by quenching, rolling and aging.
  • U.S. Patent No. 5,356,495 describes a process in which the cast strip is hot-rolled, hot-coiled and held at a hot-rolled temperature for 2-120 minutes, followed by uncoiling, quenching and cold rolling at less than 300°F, followed by recoiling the sheet.
  • the present disclosure provides a use for an aluminium alloy sheet manufactured in a continuous in-line sequence.
  • the present disclosure also provides a method for manufacturing an aluminum alloy in a continuous in-line sequence wherein the aluminum alloy is adapted and intended to be used in the manufacturing of an automobile.
  • the present disclosure also provides a use of an aluminum alloy manufactured with such a method for components in automotive manufacturing.
  • the continuous in-line sequence for manufacturing the aluminium alloy sheet comprises: (i) providing a continuously-cast thin aluminum alloy strip as feedstock; (ii) optionally, quenching the feedstock to the preferred hot or warm rolling temperature; (iii) hot or warm rolling the quenched feedstock to the desired final thickness; (iv) annealing or solution heat-treating the feedstock in-line and optionally off-line, depending on alloy and temper desired; and (v) optionally, quenching the feedstock, after which it is preferably tension- leveled and coiled.
  • This method results in an aluminum alloy sheet having the desired dimensions and properties.
  • the aluminum alloy sheet may be coiled for later use.
  • FIG. 1 shows a continuously-cast aluminum alloy strip feedstock 1 which is optionally passed through shear and trim stations 2, optionally quenched for temperature adjustment 4, hot-rolled 6, and optionally trimmed 8.
  • the feedstock may be then either annealed 16 followed by suitable quenching 18 and optional coiling 20 to produce 0 temper products 22, or solution heat treated 10, followed by suitable quenching 12 and optional coiling 14 to produce T temper products 24.
  • the annealing step 16 may be done in-line or off-line.
  • the solution heat treatment step 10 may be done in-line or off-line.
  • the temperature of the heating step and the subsequent quenching step will vary depending on the desired temper.
  • annealing refers to a heating process that causes recrystallization of the metal to occur, producing uniform formability and assisting in earing control. Typical temperatures used in annealing aluminum alloys range from about 600° to 900 ° F.
  • solution heat treatment refers to a metallurgical process in which the metal is held at a high temperature so as to cause the second phase particles of the alloying elements to dissolve into solid solution. Temperatures used in solution heat treatment are generally higher than those used in annealing, and range up to about 1060°F. This condition is then maintained by quenching of the metal for the purpose of strengthening the final product by controlled precipitation (aging).
  • feedstock refers to the aluminum alloy in strip form.
  • the feedstock employed in the practice of the present invention can be prepared by any number of continuous casting techniques well known to those skilled in the art.
  • a preferred method for making the strip is described in US 5,496,423 issued to Wyatt-Mair and Harrington.
  • Another preferred method is as described in US Patent 6,672,368 .
  • the continuously-cast aluminum alloy strip preferably ranges from about 0.06 to 0.25 inches in thickness, more preferably about 0.08 to 0.14 inches in thickness.
  • the cast strip will have a width up to about 90 inches, depending on desired continued processing and the end use of the sheet.
  • Figure 2 illustrates an as-cast microstructure of Al + 3.5% Mg alloy in transverse direction.
  • the single solid strip of Figure 2 includes three general regions, or layers, including two shell regions and center layer sandwiched therebetween.
  • continuous casting results in a strip wherein the central layer constitutes between 20 to 60 percent, optionally 20 to 30 percent, of the total thickness of the strip.
  • the molten aluminum alloy, upstream of the nip has an initial concentration of alloying elements including peritectic forming alloying elements and eutectic forming alloying elements. Alloying elements which are peritectic formers with aluminum are Ti, V, Zr and Cr.
  • All other alloying elements are eutectic formers with aluminum, such as Si, Fe, Ni, Zn, Mg, Cu and Mn.
  • dendrites typically have a lower concentration of eutectic formers than the surrounding mother melt and higher concentration of peritectic formers.
  • the small dendrites are thus partially depleted of eutectic formers while the molten metal surrounding the small dendrites is somewhat enriched in eutectic formers. Consequently, the solid central layer of the strip, which contains a large population of dendrites, is depleted of eutectic formers (typically by up to about 20 weight percent, such as about 5 to about 20 wt.
  • United States Patent No. 6,672,368 includes additional disclosure regarding continuously casting that is suitable for use in connection with this disclosure.
  • FIG. 3 there is shown schematically a preferred apparatus used in carrying out a preferred embodiment of the method of the present invention.
  • Molten metal to be cast is held in melter holders 31, 33 and 35, is passed through troughing 36 and is further prepared by optional degassing 37 and filtering 39 steps.
  • the tundish 41 supplies the molten metal to the continuous caster 45.
  • the metal feedstock 46 which emerges from the caster 45 is moved through optional shear 47 and trim 49 stations for edge trimming and transverse cutting, after which it is passed to a quenching station 51 for adjustment of rolling temperature.
  • the shear station is operated when the process in interrupted; while running, shear is open.
  • the feedstock 46 is passed through a rolling mill 53, from which it emerges at the required Final thickness.
  • the feedstock 46 is passed through a thickness gauge 54, a shapemeter 55, and optionally trimmed 57, and is then annealed or solution heat-treated in a heater 59.
  • the feedstock 46 passes through a profile gauge 61, and is optionally quenched at quenching station 63. Additional steps include passing the feedstock 46 through a tension leveler to flatten the sheet at station 65, and subjecting it to surface inspection at station 67. The resulting aluminum alloy sheet is then coiled at the coiling station 69.
  • the overall length of the processing line from the caster to the coiler is estimated at about 250 feet.
  • the total time of processing from molten metal to coil is therefore about 30 seconds.
  • 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, and the like. It is preferred 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 quench at station 51 reduces the temperature of the feedstock as it emerges from the continuous caster from a temperature of about 1000°F to the desired hot or warm rolling temperature.
  • the feedstock will exit the quench at station 51 with a temperature ranging from about 400° to 900°F, depending on alloy and temper desired. Water sprays or an air quench may be used for this purpose.
  • Hot or warm rolling 53 is typically carried out at temperatures within the range of about 400° to 1020°F, more preferably 700° to 1000°F.
  • the extent of the reduction in thickness affected by the hot rolling step of the present invention is intended to reach the required finish gauge. This typically involves a reduction of about 55%, and the as-cast gauge of the strip is adjusted so as to achieve this reduction.
  • the temperature of the sheet at the exit of the rolling station is between about 300° and 850°F, more preferably 550° to 800°F, since the sheet is cooled by the rolls during rolling.
  • the thickness of the feedstock as it emerges from the rolling station 53 will be about 0.02 to 0.15 inches, more preferably about 0.03 to 0.08 inches.
  • the heating carried out at the heater 59 is determined by the alloy and temper desired in the finished product.
  • the feedstock will be solution heat-treated in-line, at temperatures above about 950°F, preferably about 980°-1000°F. Heating is carried out for a period of about 0.1 to 3 seconds, more preferably about 0.4 to 0.6 seconds.
  • the feedstock when 0 temper is desired, will require annealing only, which can be achieved at lower temperatures, typically about 700° to 950°F, more preferably about 800°-900°F, depending upon the alloy. Again, heating is carried out for a period of about 0.1 to 3 seconds, more preferably about 0.4 to 0.6 seconds.
  • the quenching at station 63 will depend upon the temper desired in the final product.
  • feedstock which has been solution heat-treated will be quenched. preferably air and water quenched, to about 110° to 250°F, preferably to about 160°-180°F and then Coiled.
  • the quench at station 63 is a water quench or an air quench or a combined quench in which water is applied first to bring the temperature of the sheet to just above the Leidenfrost temperature (about 550°F for many aluminum alloys) and is continued by an air quench.
  • This method will combine the rapid cooling advantage of water quench with the low stress quench of air jets that will provide a high quality surface in the product and will minimize distortion.
  • an exit temperature of 200°F or below is preferred.
  • Products that have been annealed rather than heat-treated will be quenched, preferably air- and water-quenched, to about 110° to 720°F, preferably to about 680° to 700°F for some products and to lower temperatures around 200°F for other products that are subject to precipitation of intermetallic compounds during cooling, and then coiled.
  • the rolling mill arrangement for thin gauges could comprise a hot rolling step, followed by hot and/ or cold rolling steps as needed.
  • the anneal and solution heat treatment station is to be placed after the final gauge is reached, followed by the quench station. Additional in-line anneal steps and quenches may be placed between rolling steps for intermediate anneal and for keeping solute in solution, as needed.
  • the pre-quench before hot rolling needs to be included in any such arrangements for adjustment of the strip temperature for grain size control.
  • the pre-quench step is a pre-requisite for alloys subject to hot shortness.
  • FIG 4 shows schematically an apparatus for one of many alternative embodiments in which additional heating and rolling steps are carried out.
  • Metal is heated in a furnace 80 and the molten metal is held in melter holders 81, 82.
  • the molten metal is passed through troughing 84 and is further prepared by degassing 86 and filtering 88.
  • the tundish 90 supplies the molten metal to the continuous caster 92, exemplified as a belt caster, although not limited to this.
  • the metal feedstock 94 which emerges from the caster 92 is moved through optional shear 96 and trim 98 stations for edge trimming and transverse cutting, after which it is passed to an optional quenching station 100 for adjustment of rolling temperature.
  • the feedstock 94 is passed through a hot rolling mill 102, from which it emerges at an intermediate thickness.
  • the feedstock 94 is then subjected to additional hot milling 104 and cold milling 106, 108 to reach the desired final gauge.
  • the feedstock 94 is then optionally trimmed 110 and then annealed or solution heat-treated in heater 112. Following annealing/solution heat treatment in the heater 112, the feedstock 94 optionally passes through a profile gauge 113, and is optionally quenched at quenching station 114. The resulting sheet is subjected to x-ray 116, 118 and surface inspection 120 and then optionally coiled.
  • Suitable aluminum alloys for heat-treatable alloys include, but are not limited to, those of the 2XXX, 6XXX and 7XXX Series.
  • Suitable non - heat-treatable alloys include, but are not limited to, those of the 1XXX, 3XXX and 5XXX Series.
  • the present invention is applicable also to new and non-conventional alloys as it has a wide operating window both with respect to casting, rolling and in-line processing.
  • Strips of AA 5182 composition (SAL1) and 0.10 inch thickness were continuously cast in a casting apparatus as described within United States Patent No. 6, 672,368 .
  • a variation was introduced to the composition of AA 5182 by increasing the Cu content outside the AA range (SAL2) for the purpose of increasing O-temper yield strength, Table 1.
  • the strips were hot rolled in line to 0.060, 0.050 and 0.040 inch corresponding to hot reductions of 40, 50 and 60% respectively. These samples were batch annealed at temperatures between 600 and 850°F. Mechanical properties of the samples were measured by tensile tests and the yield point extension (YPE) was determined from the tensile curves following the procedure illustrated in Figure 5 .
  • YPE yield point extension
  • a thicker strip of 0.145 inch was cast and hot rolled in-line to 0.118 inch gauge (17% hot work) and batch annealed at 850°F/2hr. Samples of this coil were then cold rolled in the laboratory to 0.090, 0.060 and 0.030 inch gauge corresponding to cold work level of 25, 50 and 75% respectively. This set of cold rolled samples was batch annealed at 750°F in a laboratory furnace and was evaluated as above by tensile testing and optical microscopy. Tensile testing was done at a strain rate of 2x10 -3 s -1 using standard laboratory equipment and procedures. The sensitivity of the results to strain rate was not separately studied. For selected samples, mechanical properties and YPE were determined in three directions: longitudinal, transverse and 45 degree to the rolling direction.
  • Two families of 5182 were cast as ⁇ 0.1 inch thick strip and were hot/warm rolled in-line to different thicknesses, Table 1.
  • Samples A, B and C were selected to be within the composition limits of AA 5182 (SAL1 composition).
  • the Cu content of alloys D, G and H was increased to ⁇ 0.20% for a higher O-temper strength (composition SAL2). These latter three samples are therefore outside the AA 5182 composition limit with respect to Cu.
  • Both families of alloys were rolled in-line to 0.06, 0.05 and 0.04 inch gauge that corresponded to hot reduction of 40, 50 and 60% respectively, Table 1. All samples were batch annealed for 2 hours at several temperatures between 600 and 850°F. The progress of annealing was assessed by tensile testing, electrical conductivity measurements and microscopy.
  • Typical micrographs of fully annealed structures for 850°F are shown in Figure 9 .
  • Detailed measurement of mechanical properties and evaluation of YPE values in this batch of samples was therefore done on samples annealed at 850°F only.
  • Tensile properties of the fully annealed samples measured in the longitudinal, transverse and 45 degree directions are shown in Table 2. The properties generally showed relatively little dependence on the direction of testing.
  • the SAL2 composition did indeed increase the yield strength by about 1 ksi.
  • the YS was 20.2 ksi for sample A85 (SAL1 composition) and this increased to 21 ksi in D85 sample (SAL2).
  • the yield point elongation was evaluated from the tensile test curves only for the longitudinal direction tests, Table 3.
  • Two tensile curves, one with a YPE of 0.52% (sample D85) and the other with no YPE (sample H85), are shown in Figure 10 as examples.
  • the YPE values observed in the samples were respectively 0.46, 0.32 and 0.30% for the 0.060, 0.040 and 0.030 inch thick sheet samples of SAL1 composition. This indicated that the lowest YPE value corresponded to the lowest degree of hot rolling.
  • SAL2 composition produced somewhat higher YPE with value of 0.46% for 0.050 inch sample and 0.052% for 0.040 inch sample.
  • Table 2 Electrical conductivity of SAL1 (A, B and C) and SAL2 (D, G and H) alloys in annealed state. Processing path: hot roll in-line to gauge, Table 1.
  • Samples A, B and C are within AA 5182 composition range (SAL1). 2. Samples D, G and H contain higher level of Cu for additional strength (SAL2).
  • Table 3 Tensile properties and yield point extension (YPE) in the longitudinal direction for SAL1 (A, B and C) and SAL2 (D, G, and H) samples after furnace anneal at 850°F. The samples were prepared by in-line hot rolling only, see table 1. longitudinal tensile properties grain size hot roll gauge inch hot reduction % UTS YS elongation, % L T mean st ksi ksi total uniform ⁇ m ⁇ m ⁇ m BATCH ANNEAL 850 °F / 2 hr.
  • the continuous anneal procedure was simulated by dipping the samples of sheet in a salt pot at 1000°F for 30 seconds after which they were cooled either in still air or by quenching in water. Tensile properties and YPE measured in three directions on these samples are shown in Table 5. Regardless of the degree of prior hot reduction, method of cooling from anneal and direction of testing, the YPE values were all around 0.50%. The yield strength of the sheet also appeared to have somewhat increased by this anneal procedure. Most importantly, however, total elongation values increased from a level of ⁇ 21% to 26-28% range. A similar level of increase was noted also in the uniform elongation values, Table 5.
  • YPE Yeld point elongation
  • the grain size in the samples was found to be generally equiaxed with a mean diameter of 24 ⁇ m in the longitudinal direction and 21 ⁇ m in the thickness direction, Table 4. Representative micrographs are shown in Figure 11 .
  • the grain structure was generally equiaxed, Figure 12 and Table 6.
  • the mean grain size was 14.1 ⁇ m when measured in the thickness direction. It was somewhat larger in the rolling direction and transverse direction, 19.4 and 20.2 ⁇ m, respectively.
  • the mean grain size for this sheet was taken as 17.9 ⁇ m, the average of the three measurements.
  • batch anneal was done on material cold rolled from 0.118 inch thick feedstock that had been made by in-line hot rolling ( ⁇ 19%) in the plant from an as-cast strip of 0.145 inch thickness.
  • the hot rolled sheet had a mean grain size of 38 ⁇ m and produced a YPE value of 0.38% when tested in the longitudinal direction after a simulated batch anneal at 850°F/2 hr, Table 7 and Figure 13 .
  • YPE in the transverse and 45 degree directions were too small for accurate measurement.
  • the hot rolled and annealed sheet was then cold rolled by 25, 50 and 75% after which a final anneal was done at 750 F/2h.
  • the grain sizes were 28, 17 and 12 ⁇ m ( Figure 13 ) and YPE in the longitudinal direction were respectively 0.34, 0.97 and 1.34%, Table 7.
  • the yield stress of the cold worked samples increased from 16.4 ksi to 17.1 for 25% cold rolling, and to 19.1 and 20.7 ksi for 50 and 75% rolled materials, respectively.
  • the sheet evaluated was hot rolled in line from ingot to 0.135 inch gauge (3.43 mm) and then cold rolled by 56% to 1.5 mm thickness (0.060 inch) and was batch annealed at 750°F/2 hr.
  • the grains were equiaxed with a mean size of 17 ⁇ m, Figure 14 .
  • This sheet was characterized for YPE in three directions, Table 8.
  • Table 6 Grain size measurements from cast 110509. Manufacturing path: in-line hot roll from 0.116 inch as-cast gauge to 0.070 inch, cold roll to 0.040 inch, continuous anneal in Danville line at 1000°F.
  • Hot roll gauge 0.135 inch, cold roll to final gauge (53%), furnace anneal at 750°F/2 hr. test direction TYS UTS elongation grain size YPE test gauge inch total uniform ksi ksi % % ⁇ m % 879934-L1 0.0642 L 19.36 41.95 22.72 22.39 17 0.78 879934-L2 0.0643 19.19 41.93 18.67 18.25 17 0.73 879934-45-1 0.0644 45 degree 18.48 39.91 27.19 26.90 17 0.95 879934-45-2 0.0644 18.41 39.48 26.60 26.29 17 0.98 879934-LT1 0.0646 T 19.17 40.12 25.6 25.30 17 1.02 879934-LT2 0.0645 19.40 40.32 24.18 23.86 17 1.04
  • the longitudinal direction provided the lowest YPE values of 0.78 and 0.73 % in two samples. Highest YPE values were observed in the transverse direction that had a mean value of 1.03%. An intermediate value of 0.97 was measured in the 45 degree direction. These values are considered typical for AA 5182 made from ingot following regular plant practices for hot and cold rolling.
EP13178860.6A 2012-08-16 2013-08-01 Procédé de fabrication d'un alliage d'aluminium destiné à être utilisé dans la construction automobile Active EP2698216B1 (fr)

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Cited By (5)

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CN104942104A (zh) * 2015-05-05 2015-09-30 北京科技大学 一种非等厚u肋热辊压成形工艺
CN106044095A (zh) * 2016-08-19 2016-10-26 宁波萨科森工业科技有限公司 一种新型铝箔退火炉进料料车
WO2018063024A1 (fr) * 2016-09-30 2018-04-05 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Procédé de production de produits semi-finis déformés à partir d'alliages à base d'aluminium
US11554443B2 (en) 2016-01-14 2023-01-17 Howmet Aerospace Inc. Methods for producing forged products and other worked products
WO2023031334A1 (fr) * 2021-09-03 2023-03-09 Speira Gmbh Bande d'alliage d'aluminium optimisée pour le formage, et son procédé de fabrication

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US20050211350A1 (en) * 2004-02-19 2005-09-29 Ali Unal In-line method of making T or O temper aluminum alloy sheets

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WO1998040528A1 (fr) * 1997-03-07 1998-09-17 Alcan International Limited Procede de production de tole aluminiee
US20030150587A1 (en) * 2002-02-11 2003-08-14 Zhong Li Process for producing aluminum sheet product having controlled recrystallization
US20050211350A1 (en) * 2004-02-19 2005-09-29 Ali Unal In-line method of making T or O temper aluminum alloy sheets

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104942104A (zh) * 2015-05-05 2015-09-30 北京科技大学 一种非等厚u肋热辊压成形工艺
US11554443B2 (en) 2016-01-14 2023-01-17 Howmet Aerospace Inc. Methods for producing forged products and other worked products
CN106044095A (zh) * 2016-08-19 2016-10-26 宁波萨科森工业科技有限公司 一种新型铝箔退火炉进料料车
WO2018063024A1 (fr) * 2016-09-30 2018-04-05 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Procédé de production de produits semi-finis déformés à partir d'alliages à base d'aluminium
CN109790612A (zh) * 2016-09-30 2019-05-21 俄铝工程技术中心有限责任公司 由铝基合金生产变形的半成品的方法
EA037441B1 (ru) * 2016-09-30 2021-03-29 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Способ получения деформированных полуфабрикатов из сплавов на основе алюминия
CN109790612B (zh) * 2016-09-30 2021-10-22 俄铝工程技术中心有限责任公司 由铝基合金生产变形的半成品的方法
WO2023031334A1 (fr) * 2021-09-03 2023-03-09 Speira Gmbh Bande d'alliage d'aluminium optimisée pour le formage, et son procédé de fabrication

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