EP2698216B1 - 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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EP2698216B1
EP2698216B1 EP13178860.6A EP13178860A EP2698216B1 EP 2698216 B1 EP2698216 B1 EP 2698216B1 EP 13178860 A EP13178860 A EP 13178860A EP 2698216 B1 EP2698216 B1 EP 2698216B1
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strip
annealing
continuously
hot
aluminum alloy
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German (de)
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EP2698216A1 (fr
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David A. Tomes, Jr.
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Arconic Technologies LLC
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Arconic Technologies LLC
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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.
  • 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 7.62 to 121.92 meters per minute; alternatively from 15.24 meters per minute to 106.68 meters 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 176.67°C.
  • U.S. Patent No. 5,772,802 describes a method in which the aluminum alloy cast strip is quenched, rolled, annealed at temperatures between 315.56° and 648.89°C 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 148.89°C, followed by recoiling the sheet.
  • US 2005/0211350 A1 relates to a method of making aluminum alloy sheet in a continuous in-line process is provided.
  • 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 having the desired properties, in a much shorter processing time.
  • the T or O temper may be selected by annealing the strip to achieve an O temper or solution heat treating the strip to achieve a T temper, and, if a T temper is desired, quenching the strip subsequent to the solution heat treating.
  • the invention further provides a hot or warm rolling step wherein the strip is substantially reduces to a final thickness about 10-65% from a casting thickness.
  • WO 1998/40528 A1 relates to a process of producing an aluminum alloy sheet article of high yield strength and ductility suitable, in particular, for use in manufacturing automotive panels.
  • the process comprises casting a non heat-treatable aluminum alloy to form a cast slab, and subjecting said cast slab to a series of rolling steps to produce a sheet article of final gauge, preferably followed by annealing to cause recrystallization.
  • the rolling steps involve hot and warm rolling the slab to form an intermediate sheet article of intermediate gauge, cooling the intermediate sheet article, and then warm and cold rolling the cooled intermediate sheet to final gauge at a temperature in the range of ambient temperature to 340°C to form said sheet article.
  • the series of rolling steps is carried out continuously without intermediate coiling or full annealing of the intermediate sheet article.
  • the invention also relates to the alloy sheet article produced by the process.
  • the present invention relates to a method for manufacturing an aluminum alloy in a continuous in-line sequence as defined by independent claim 1, wherein further developments of the inventive method are provided in the sub-claims, respectively.
  • 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 is then annealed 16 followed by suitable quenching 18 and optional coiling 20 to produce 0 temper products 2.
  • the annealing step 16 may be done in-line or off-line. As can be seen in Figure 1 , the temperature of the heating step and the subsequent quenching step will vary depending on the desired temper.
  • anneal 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 315.56° to 482.22°C.
  • 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 571.11°C. 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 0.1524 to 0.635 cm in thickness, more preferably about 0.2032 to 0.3556 cm in thickness.
  • the cast strip will have a width up to about 228.6 cm, 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 76.2 meters.
  • 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 537.78°C to the desired hot or warm rolling temperature.
  • the feedstock will exit the quench at station 51 with a temperature ranging from about 204.44° to 482.22°C, 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 204.44° to 548.89°C, more preferably 371.11° to 537.78°C.
  • 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 148.89° and 454.44°C, more preferably 287.78° to 426.67°C, 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 0.0508 to 0.381 cm, more preferably about 0.0762 to 0.2032 cm.
  • 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 510°C, preferably about 526.67°-537.78°C. 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, the feedstock will require annealing only, which can be achieved at lower temperatures, typically about 371.11° to 510°C, more preferably about 426.67°-482.22°C, 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 43,33° to 121.11°C, preferably to about 71.11°-82.22°C 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 287.78°C 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 93.33°C or below is preferred.
  • Products that have been annealed rather than heat-treated will be quenched, preferably air- and water-quenched, to about 43.33° to 382.22°C, preferably to about 360° to 371.11°C for some products and to lower temperatures around 93.33°C 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 in heater 112. Following annealing 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.
  • Strips of AA 5182 composition (SAL1) and 0.254 cm 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 0.1524, 0.127 and 0.1016 cm corresponding to hot reductions of 40, 50 and 60% respectively. These samples were batch annealed at temperatures between 315.56° and 454.44°C. 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 .
  • One coil of AA 5182 composition was processed to test gauge by cold rolling. It had been hot rolled in-line from 0.29464 cm to 0.1778 cm thickness after which it was cold rolled to test gauge of 0.1016 cm. The annealing was done in a continuous heat treat line at 537.78°C after which it was forced air cooled. This coil had a cold work of 43% prior to annealing. Tensile testing and microscopy were carried out on samples of the coil.
  • a thicker strip of 0.3683 cm was cast and hot rolled in-line to 0.29972 cm gauge (17% hot work) and batch annealed at 454.44°C/2h. Samples of this coil were then cold rolled in the laboratory to 0.2286, 0.1524 and 0.0762 cm gauge corresponding to cold work level of 25, 50 and 75% respectively. This set of cold rolled samples was batch annealed at 398.89°C 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 cm 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 0.1524, 0.127 and 0.1016 cm 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 315.56 and 454.44°C. The progress of annealing was assessed by tensile testing, electrical conductivity measurements and microscopy.
  • Typical micrographs of fully annealed structures for 454.44°C 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 454.44°C 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 139.274 MPa for sample A85 (SAL1 composition) and this increased to 144.790 MPa 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 0.1524, 0.1016 and 0.0762 cm 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 0.127 cm sample and 0.052% for 0.1016 cm 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 anneal gauge, cm sample 0.1016 A 0.127 B 0.1524 C 0.1016 D 0.127 G electrical conductivity, % IACS AR as rolled 24.9 24.7 24.3 24.8 24.6 600 batch 315.56/2hr 26.8 26.4 25.9 26.7 26.5 650 batch 343.33/2hr 28.4 28.1 27.7 28.4 28.4 700 batch 371.11/2hr 29.4 29.3 28.8 29.7 29.6 750 batch 398.89/2hr 29.5 29.6 29.1 29.9 29.8 800 batch 426.67/2hr 29.5 29.4 29.1 29.8 29.7 850 batch 454.44/hr 29.4 29.4 29.6 29.4
  • 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, Band C) and SAL2 (D, G, and H) samples after furnance anneal at 454.44°C. The samples were prepared by in-line hot rolling only, see Table 1.
  • the continuous anneal procedure was simulated by dipping the samples of sheet in a salt pot at 537.78°C 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.
  • Table 5 Yield point elongation (YPE) after simulated continous anneal (537.78°C /30s) of material hot rolled in-line to gauge in comparison with material cold rolled by 43% and then continous annealed in coil form in Danville longitudinal transverse 45 degree alloy hot roll gauge flash anneal cooling method UTS YS elongation, % YPE UTS YS elongation, % YPE UTS YS elongation, % YPE cm MPa MPa total uniform % MPa MPa total uniform % MPa MPa total uniform % SAL1 0.1524 537.78'C water 303.36931 144.7899 27.5 24.5 0.52 302.679832 146.168848 26.5 22.1 0.56 296.474551 142.032 27.5 22.8 0.53 SAL1 0.1524 30s quench 302.67983 146.16885 26.2 21.8 0.54 304.058784 148.926751 27.8 23.1
  • 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 0.29972 cm thick feedstock that had been made by in-line hot rolling ( ⁇ 19%) in the plant from an as-cast strip of 0.3683 cm 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 454.44°C/2 h, 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 298.89°C/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 113.07 MPa to 117.90 MPa for 25% cold rolling, and to 131.69 MPa and 142.72 MPa for 50 and 75% rolled materials, respectively.
  • the sheet evaluated was hot rolled in line from ingot to 0.3429 cm gauge (3.43 mm) and then cold rolled by 56% to 1.5 mm thickness (0.1524 cm) and was batch annealed at 398.89°C/2 h.
  • 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 0.295 cm as cast gauge to 0.178 cm cold roll to 0.1016 cm, continuous anneal in Danville line at 537.78°C.
  • Hot roll gauge 0.3429 cm, cold roll to final gauge (53%), furnance anneal at 398.89°C. test direction elongation test gauge cm TYS MPa UTS MPa total % uniform % grain size ⁇ m YPE 879934-L1 0.163068 L 133.482496 289.23506 22.72 22.39 17 0.78 879934-L2 0.163322 132.310387 289.09716 18.67 18.25 17 07.3 879934-45-1 0.163576 45 degree 127.415109 275.16975 27.19 26.90 17 09.5 879934-45-2 0.163576 126.932476 272.20501 26.60 26.29 17 09.8 879934-LT1 0.164084 T 132.172492 276.61765 25.60 25.30 17 10.2 879934-LT2 0.16383 133.758286 277.9966 24.18 23.86 17 10.4
  • 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.

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Claims (11)

  1. Procédé de fabrication d'un alliage d'aluminium dans une séquence continue en ligne, comprenant :
    i) la fourniture d'une bande mince d'alliage d'aluminium coulée en continu ;
    ii) le laminage à chaud en ligne de la bande coulée en continu ; et
    iii) le recuit de la bande coulée en continu laminée à chaud jusqu'à l'état O ayant un allongement de limite d'élasticité apparente inférieur à 0,6 %,
    dans lequel l'alliage d'aluminium est utilisé dans la fabrication d'une automobile, caractérisé en ce que la bande coulée en continu est coulée dans un appareil de coulée continue entre deux cylindres horizontaux, l'appareil de coulée continue entre deux cylindres horizontaux ayant un pincement formé entre deux cylindres de coulée, et dans lequel pendant la coulée, un point de solidification complète de l'alliage Al-Mg est formé au niveau du pincement, de telle sorte que le composant est exempt de marques de contrainte d'étirement, dans lequel l'alliage d'aluminium est un alliage Al-Mg et plus précisément un alliage AA5182 ayant une teneur renforcée en Cu de 0,2 %, dans lequel la bande coulée en continu a une épaisseur allant de 0,1524 à 0,635 cm avant le laminage à chaud, dans lequel pendant le laminage à chaud en ligne, l'épaisseur de la bande coulée en continu est réduite de 40, 50 % ou 60 %, et dans lequel le recuit de la bande coulée en continu laminée à chaud est effectué entre 315,56 et 454,44 °C pendant 2 heures.
  2. Procédé selon la revendication 1,
    dans lequel le recuit de la première bande coulée en continu laminée à chaud est effectué en ligne.
  3. Procédé selon la revendication 1,
    dans lequel le recuit de la bande coulée en continu laminée à chaud est effectué hors ligne.
  4. Procédé selon la revendication 1 ou 2,
    dans lequel après le recuit, la bande a une taille moyenne de grain inférieure à 50 micromètres, de préférence inférieure à 30 micromètres, et de manière davantage préférée inférieure à 25 micromètres.
  5. Procédé selon l'une des revendications 1 à 4,
    dans lequel après le recuit, la bande a une taille moyenne de grains entre 25 et 50 micromètres.
  6. Procédé selon l'une des revendications 1 à 4,
    dans lequel après le recuit, la bande a une taille moyenne de grains entre 5 et 25 micromètres.
  7. Procédé selon l'une des revendications 1 à 6,
    dans lequel la bande coulée en continu a une épaisseur de 0,254 cm avant le laminage à chaud.
  8. Procédé selon l'une des revendications 1 à 7,
    dans lequel un allongement de limite d'élasticité apparente après l'étape de recuit est inférieur à 0,6 % et de préférence entre 0,3 % et 0,52 %.
  9. Procédé selon l'une des revendications 1 à 8,
    dans lequel l'étape de recuit est effectuée à 454,44 °C pendant 2 heures.
  10. Procédé selon l'une des revendications 1 à 9,
    dans lequel la bande coulée en continu est laminée à chaud jusqu'à une épaisseur entre 0,1016 cm et 0,1524 cm.
  11. Utilisation d'un alliage d'aluminium fabriqué avec un procédé selon l'une des revendications 1 à 10 pour des composants dans la fabrication d'automobiles.
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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CN104942104B (zh) * 2015-05-05 2017-02-22 北京科技大学 一种非等厚u肋热辊压成形工艺
RU2702888C1 (ru) 2016-01-14 2019-10-11 Арконик Инк. Способы получения кованых изделий и других обработанных изделий
CN106044095B (zh) * 2016-08-19 2018-05-15 宁波萨科森工业科技有限公司 一种铝箔退火炉进料料车
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
JP2024534911A (ja) * 2021-09-03 2024-09-26 スペイラ ゲゼルシャフト ミット ベシュレンクテル ハフツング 成形のために最適化されたアルミニウム合金ストリップおよび製造のための方法

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US6672368B2 (en) * 2001-02-20 2004-01-06 Alcoa Inc. Continuous casting of aluminum

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US6391127B1 (en) * 1992-06-23 2002-05-21 Alcoa Inc. Method of manufacturing aluminum alloy sheet
DE69808738T2 (de) * 1997-03-07 2003-06-26 Alcan International Ltd., Montreal Verfahren zur herstellung eines aluminiumbleches
US6789602B2 (en) * 2002-02-11 2004-09-14 Commonwealth Industries, Inc. 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

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US6672368B2 (en) * 2001-02-20 2004-01-06 Alcoa Inc. Continuous casting of aluminum

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