EP3740598B1 - Alliage d'aluminium, méthode de fabrication d'un produit plat d'aluminium, le produit plat d'aluminium et utilisation - Google Patents

Alliage d'aluminium, méthode de fabrication d'un produit plat d'aluminium, le produit plat d'aluminium et utilisation Download PDF

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EP3740598B1
EP3740598B1 EP19701587.8A EP19701587A EP3740598B1 EP 3740598 B1 EP3740598 B1 EP 3740598B1 EP 19701587 A EP19701587 A EP 19701587A EP 3740598 B1 EP3740598 B1 EP 3740598B1
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Prior art keywords
aluminium
aluminum
content
flat product
forming
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German (de)
English (en)
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EP3740598A1 (fr
EP3740598C0 (fr
Inventor
Werner Droste
Olaf Engler
Katrin Kuhnke
Simon Miller-Jupp
Michael RÖSNER-KUHN
Reinhard Pritzlaff
Martin Christoph Lentz
David Goddard
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Speira GmbH
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Speira GmbH
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D3/00—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts
    • B21D3/02—Straightening or restoring form of metal rods, metal tubes, metal profiles, or specific articles made therefrom, whether or not in combination with sheet metal parts by rollers
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • 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 invention relates to an aluminum alloy for superplastic aluminum flat products, a method for producing a superplastic aluminum flat product, a superplastic aluminum flat product and its use.
  • a typical process for superplastic forming is, for example, so-called blow molding, in which a sheet-like starting material is pressed by pressurizing it with a fluid, in particular a gas, into a die that has a negative shape to the shape to be produced.
  • a fluid in particular a gas
  • superplastic forming is classically performed at low strain rates on the order of 10 -4 s -1
  • recent developments are moving towards high-speed superplastic forming with very high strain rates.
  • the alloy AA 5083 is known, which can be used for the manufacture of products by means of superplastic forming.
  • the object of the present invention is to provide an aluminum alloy, a method for producing an aluminum flat product and an aluminum flat product which has improved properties in superplastic forming.
  • the aluminum alloy can be used to produce an aluminum product by superplastic forming an aluminum flat product from the aluminum alloy.
  • the Na content of the aluminum alloy is at most 2 ppm (ie at most 0.0002% by weight), preferably at most 1.4 ppm, in particular at most 1.0 ppm. It was found that the sodium content in the aluminum alloy must be kept extremely low, otherwise edge cracks can occur during hot rolling of the ingot. This is especially true since the Aluminum alloy has a high Mg content of 5.2% by weight or more. In order to achieve the low Na contents mentioned above, the melt can be treated with chlorine, for example.
  • an aluminum flat product in particular a superplastic aluminum flat product, in which an aluminum melt is provided from the aluminum alloy mentioned in claim 1, in which the aluminum melt is cast into an ingot, in which the ingot a hot strip, in which the hot strip is cold-rolled into a cold strip and in which the cold strip is straightened.
  • an aluminum flat product in particular a superplastic aluminum flat product, which can be produced or has been produced using the method described above.
  • the above-mentioned object is also achieved according to the invention by using the aluminum flat product described above for producing an aluminum product by superplastic forming of the aluminum flat product, in particular by means of blow molding.
  • a superplastic aluminum flat product can be produced that is particularly well suited for superplastic forming.
  • a heat treatment of the aluminum flat product when it is heated to the forming temperature for superplastic forming leads to the formation of a fine structure, so that high degrees of forming can be achieved without defects.
  • the forming temperature is preferably in the range from 450.degree. C. to 520.degree.
  • the total elongation during superplastic forming is preferably at least 100%.
  • a strain rate sensitivity m ⁇ 0.3 is typically only achieved in a specific strain rate range, for example in the range from 10 -4 s -1 to 10 -3 s -1 , in which the flat aluminum product is superplastic.
  • the method is used to produce an aluminum flat product.
  • the aluminum flat product can in particular be a strip or a sheet.
  • an aluminum melt is provided from the aluminum alloy described above.
  • the aluminum melt is provided in particular by the fact that the composition of the aluminum alloy described above is adjusted in an aluminum furnace by melting down primary aluminum, optionally scrap and other additives.
  • the aluminum melt provided is cast into an ingot, in particular in DC (direct chill) continuous casting.
  • the ingot is preheated for hot rolling.
  • a separate billet homogenization can be carried out before preheating in order to obtain a more uniform structure.
  • the ingot is then hot-rolled to form a hot strip, preferably at a temperature in the range from 280° C. to 550° C., in particular a hot strip temperature (ie at the final hot strip thickness) in the range from 280° C. to 350° C. is set.
  • the hot strip is then cold-rolled into a cold strip.
  • the cold strip After cold rolling, the cold strip is straightened. When straightening the cold strip, the cold strip is guided through a plurality of straightening rolls which are offset from one another in order to achieve a flatness suitable for superplastic forming.
  • Various embodiments of the aluminum alloy, the method, the aluminum flat product and its use are described below, with the individual embodiments each applying individually to the aluminum alloy, the method, the aluminum flat product and the use. Furthermore, the individual embodiments can also be combined with one another.
  • the aluminum melt has an Si content of 0.03-0.10% by weight and an Fe content of 0.05-0.15% by weight.
  • Silicon and iron are dispersoid formers and are therefore fundamentally advantageous for achieving a fine grain structure for superplastic forming.
  • silicon and iron can form coarse intermetallic phases, in particular AlSiFeMn phases, with a size of more than 20 ⁇ m or even more than 30 ⁇ m, which lead to pore formation during superplastic forming and thus in particular the mechanical ones Affect properties of the aluminum product made from the aluminum flat product. Therefore, the Si content of the aluminum alloy is preferably limited to 0.10% by weight, and the Fe content of the aluminum alloy is preferably limited to 0.15% by weight.
  • a silicon content below 0.03% by weight or an iron content below 0.05% by weight can only be achieved with great effort in technical aluminum alloys, which would significantly increase the production costs of the aluminum flat product and the aluminum product made from it.
  • silicon and iron contents in the ranges mentioned it was found that with the silicon and iron contents in the ranges mentioned, a fine grain structure for superplastic forming can be achieved with an acceptably low level of pore formation during superplastic forming.
  • the Cu content of the aluminum alloy is at most 0.05% by weight. In this way the corrosion resistance of the alloy is not adversely affected. In addition, the low Cu content keeps the yield stress low at elevated temperatures, which has a positive effect on superplastic forming.
  • the aluminum alloy has a Mn content of 0.7% to 1.0% by weight. It was found that manganese acts as a strong dispersoid former in the aluminum alloy, so that a higher manganese content of at least 0.7% by weight produces a high number or density of fine dispersoids in the aluminum flat product. It was found that these manganese dispersoids impede grain growth, so that after superplastic forming of an aluminum flat product made from the aluminum alloy, a fine-grained structure is present despite the high forming temperatures.
  • the aluminum alloy has a magnesium content of 5.2% by weight to 5.5% by weight. It was found that an increased magnesium content of at least 5.2% by weight can stabilize the grain sizes, which further improves the superplastic properties of the aluminum flat product. Furthermore, due to the increased magnesium content in the range mentioned, improved strength is achieved with still good rollability. In particular, the magnesium content in this range improves the strength of an aluminum product made from the aluminum flat product after superplastic working.
  • the aluminum alloy has a zinc content of at most 0.06% by weight and/or a titanium content in the range of 0.015-0.03% by weight. It has been found that a zinc content of up to 0.06% by weight and a titanium content of up to 0.03% by weight do not adversely affect the properties for the Superplastic forming of the aluminum flat product affects. Titanium content is desirable even to a limited extent as a grain refiner, particularly at a level of at least 0.015% by weight.
  • the aluminum alloy has a boron content of at most 50 ppm (i.e. at most 0.005% by weight) and/or a calcium content of at most 15 ppm (i.e. at most 0.0015% by weight) and/or a lithium content of a maximum of 15 ppm (i.e. a maximum of 0.0015% by weight).
  • Titanium borides have a grain-refining effect during casting and thus have a beneficial effect on the rolling process and the homogeneity of the product, with a maximum boron content of 50 ppm not having a negative effect on the properties for the superplastic forming of the aluminum flat product.
  • calcium and lithium promote the formation of edge cracks and thereby impair rollability, particularly during hot rolling.
  • the aluminum melt is provided in that a preliminary aluminum melt is melted together with additives in order to achieve the composition of the aluminum melt to be provided, in particular the composition described above, with at least two of the alloying elements Cr, Mn and Ti, preferably all three alloying elements Cr, Mn and Ti, are charged separately from each other.
  • the starting material In order to produce an aluminum melt with a specific alloy composition from the starting material, for example primary aluminum and/or aluminum scrap, the starting material is first melted down in a melting furnace to form a preliminary aluminum melt and then - typically after pre-calculated charging - with suitable additives, in particular from alloy metal, master alloys, scrap and/or suitable additives, are fused to achieve the desired alloy composition.
  • suitable additives in particular from alloy metal, master alloys, scrap and/or suitable additives
  • the formation of these coarse particles can be prevented by charging at least two of the alloying elements Cr, Mn and Ti, preferably all three alloying elements Cr, Mn and Ti, separately from one another.
  • the separate charging of two alloying elements means that the additives to be added to adjust the desired content of one of the two alloying elements and the additives to be added to adjust the desired content of the other of the two alloying elements are added at different points in time to the preliminary aluminum melt. If, for example, titanium boride rods are to be added to the preliminary aluminum melt to adjust the Ti content and pieces of a Mn-containing master alloy are to be added to adjust the Mn content, the titanium boride rods and the pieces of the master alloy are preferably melted together with the temporary aluminum melt at separate times.
  • Mixing of the aluminum melt in the melting furnace preferably takes place between the addition of the additives for a first of the alloying elements Cr, Mn and Ti and the addition of the additives for a second of the alloying elements Cr, Mn and Ti.
  • the preliminary aluminum melt is mixed in the melting furnace until an aluminum melt with a homogeneous composition is obtained.
  • the homogeneity of the preliminary Aluminum melt in the melting furnace is sufficient if the chemical analysis of the melt agrees with the charge for the first of the alloying elements Cr, Mn and Ti. Sampling to determine homogeneity is preferably carried out in three different areas of the melting furnace. Accordingly, in the above example, after the addition of titanium boride and before the addition of the master alloy pieces, the preliminary aluminum melt is preferably homogenized by stirring until a consistent Ti content has been achieved in three different zones of the melting furnace.
  • the content of the second of the alloying elements Cr and Mn during the charging of the first of the alloying elements Cr and Mn in the preliminary Aluminum melt preferably max. 0.05% by weight. If, for example, Mn is charged first and then Cr, the Cr content in the aluminum melt during the charging of Mn is preferably a maximum of 0.05% by weight. This has turned out to be advantageous in order to counteract the formation of coarse particles.
  • the temperature of the preliminary aluminum melt when charging Cr is preferably more than 740°C, in particular at least 750°C. In this way, Cr can be distributed very evenly in the aluminum melt.
  • Mg is preferably charged first after Cr, Mn and/or Ti, preferably as the last element. Furthermore, the temperature of the preliminary aluminum melt when charging Mg is preferably less than 740°C, in particular max. 730°C. In this way, the desired Mg content can be set better, since the Mg content can be reduced by burn-off at higher temperatures or when alloying is added prematurely.
  • a proportion of scrap of less than 5% by weight, preferably less than 1% by weight, in particular less than 0.1% by weight, is used to provide the aluminum melt. It was found that even small amounts of certain accompanying elements and impurities from the scrap portion can lead to the formation of large particles in the aluminum melt and in the aluminum flat product made from it, which as nucleating agents contribute to the formation of pores and thus to damage during superplastic forming. Therefore, the proportion of scrap in the production of the aluminum melt is preferably kept as low as possible, or preferably even no scrap is added at all. Accordingly, the aluminum melt is preferably provided in particular by essentially melting down primary aluminum, optionally with additives, in order to obtain the desired composition.
  • the degree of rolling during cold rolling is in the range from 70% to 80% overall.
  • the aluminum flat product is in the H18 state, preferably in the H19 state according to DIN EN 515. Due to the high degree of deformation during cold rolling, a high dislocation density is introduced into the material. As a result, the material of the aluminum flat product spontaneously recrystallizes with a very fine microstructure during the heating for the superplastic forming, which is advantageous for the superplastic forming.
  • the cold rolling is carried out without intermediate annealing. If an intermediate anneal is nevertheless carried out, the above-mentioned degree of reduction during cold rolling refers to the total degree of reduction after the last intermediate anneal.
  • the final thickness of the cold strip is preferably in the range of 1-3 mm.
  • the Hot strip thickness preferably in the range from 3 to 15 mm, in particular in the range from 4 to 12 mm.
  • the degree of rolling in the last cold rolling pass is preferably less than 33%.
  • the H18 and H19 states can be produced without causing any adverse effects on the superplastic forming.
  • surface defects, in particular chatter marks are avoided by limiting the degree of rolling in the last pass.
  • the cold strip is straightened using straightening rolls with a diameter of more than 60 mm. It has been found that using larger straightening rolls can avoid unwanted surface defects after superplastic forming.
  • the cold strip is cut into sheet metal after straightening without being rolled up in the meantime.
  • the evenness of the strip achieved by straightening is not deteriorated again, so that a second straightening process is unnecessary.
  • the cold strip has been straightened using straightening rolls with a diameter of more than 60 mm, thereby reducing or even avoiding surface defects. In this way, the possible introduction of surface defects in a second straightening process, which may be carried out by the customer, can be avoided.
  • the temperature of the strip is kept in the range below 200.degree. C., preferably below 50.degree. C., in particular at room temperature of, for example, approx. 20.degree. In this way, premature recovery due to the reduction of the dislocations introduced into the aluminum flat product by cold rolling is avoided, so that a strong recrystallization effect with fine structure formation can only occur when the sheet metal is heated for superplastic forming.
  • the aluminum flat product has a yield point R p0.2 of at least 160 MPa, in particular at least 170 MPa, and a tensile strength R m of at least 310 MPa, in particular at least 320 MPa, after heat treatment for 30 minutes at 500° C.
  • R p0.2 and R m must each be determined in a tensile test according to DIN EN ISO 6892-1:2017.
  • the aluminum flat product after superplastic forming at a forming temperature of 515° C., a strain rate of 2.5 ⁇ 10 -4 s -1 and a total strain of 100%, the aluminum flat product preferably has a porosity of less than 1.5%, in particular less than 1% up.
  • the process described above in particular a maximum Fe content of 0.15% by weight and a maximum Si content of 0.10% by weight and the preferably separate charging of Mn, Cr and preferably also Ti can avoid the formation of coarse particles in the aluminum flat product, which lead to pore formation during superplastic forming.
  • the process can be used to produce aluminum flat products that have very low porosity after superplastic forming.
  • the low porosity after the superplastic forming in particular combined with a Mn content of at least 0.7% by weight and a Mg content of at least 5.2% by weight, also leads to very good mechanical properties of the aluminum flat product a heat treatment caused by the typical forming temperatures of superplastic forming. This means that aluminum products with very low porosity and very good mechanical properties can be produced from the aluminum flat products by superplastic forming.
  • the aluminum flat product has an average grain diameter of at most 15 ⁇ m after heat treatment at 500° C. for 5 minutes.
  • the mean grain diameters are to be determined according to ASTM E112. It was found that the process described above can be used to produce an aluminum flat product which, after a short heat treatment has a correspondingly fine structure due to the setting of a typical forming temperature for superplastic forming. This is achieved in particular with the Mg content of at least 5.2% by weight, the preferred Cr content between 0.12 and 0.18% by weight, the Si content of at most 0.10% by weight, the preferred Fe content of maximum 0.05% by weight, achieved by the separate charging of Mn, Cr and/or Ti and by the preferred H19 condition of the aluminum flat product.
  • the superplastic forming is carried out with a strain rate of more than 10 -3 s -1 , in particular of at least 10 -2 s -1 .
  • superplastic forming occurs at strain rates in the range of 10 -4 to 10 -3 s -1 .
  • the aluminum flat products produced with the described method can be superplastically formed with significantly higher strain rates without the material constricting during the forming. This is achieved in particular by a strain rate sensitivity of m ⁇ 0.3 even at higher strain rates of over 10 -3 s -1 .
  • the aluminum flat product has a strain rate sensitivity m, determined by means of the incremental strain rate test according to Lederich ( Lederich et al.
  • figure 1 shows an exemplary embodiment of the method for producing an aluminum flat product in a schematic representation.
  • a preliminary aluminum melt is first produced by adding primary metal 4 and alloying additives 6 to an aluminum melting furnace 8 and melting them down there.
  • the use of aluminum scrap is preferably largely dispensed with for the production of the preliminary aluminum melt 10 .
  • the preliminary aluminum melt 10 is homogenized in the melting furnace 8, which is figure 1 is illustrated by the agitator 14 shown schematically.
  • the homogenized preliminary aluminum melt 10 in the aluminum melting furnace 8 has the following composition: 0.03% by weight ⁇ si ⁇ 0.10% by weight, 0.05% by weight ⁇ feet ⁇ 0.15% by weight, Cu ⁇ 0.05% by weight, 0.7% by weight ⁇ Mn ⁇ 1.0% by weight, mg ⁇ 1% by weight, Cr ⁇ 0.05% by weight, Zn ⁇ 0.06% by weight, 0.015% by weight ⁇ Ti ⁇ 0.030%, N / A ⁇ 1.0ppm, unavoidable impurities individually up to a maximum of 0.05% by weight, in total a maximum of 0.15% by weight, remainder aluminum.
  • the low Na content can be achieved, for example, by treating the melt with chlorine.
  • the homogenized aluminum melt 22 has the following composition: 0.03% by weight ⁇ si ⁇ 0.10% by weight, 0.05% by weight ⁇ feet ⁇ 0.15% by weight, Cu ⁇ 0.05% by weight, 0.7% by weight ⁇ Mn ⁇ 1.0% by weight, mg ⁇ 1% by weight, 0.12% by weight ⁇ Cr ⁇ 0.18% by weight, Zn ⁇ 0.06% by weight, 0.015% by weight ⁇ Ti ⁇ 0.030%, N / A ⁇ 1.0ppm, unavoidable impurities individually up to a maximum of 0.05% by weight, in total a maximum of 0.15% by weight, remainder aluminum.
  • steps 2, 12 and 16 described separate charging of Mn or Ti and Cr is achieved.
  • the Mn content and the Ti content are first set, while the material 18 to be added separately for setting the desired Cr content is only added in the third step 16 after the preliminary melt 10 has been homogenized in step 12.
  • Ti can also be charged separately from Mn.
  • the content of other alloying elements in particular Si and Fe
  • the charging of these alloying elements can take place simultaneously or separately from one another.
  • the homogenized aluminum melt 25 has the following composition: 0.03% by weight ⁇ si ⁇ 0.10% by weight, 0.05% by weight ⁇ feet ⁇ 0.15% by weight, Cu ⁇ 0.05% by weight, 0.7% by weight ⁇ Mn ⁇ 1.0% by weight, 5.2% by weight ⁇ mg ⁇ 5.5% by weight, 0.12% by weight ⁇ Cr ⁇ 0.18% by weight, Zn ⁇ 0.06% by weight, 0.015% by weight ⁇ Ti ⁇ 0.030%, N / A ⁇ 1.0ppm, unavoidable impurities individually up to a maximum of 0.05% by weight, in total a maximum of 0.15% by weight, remainder aluminum.
  • Mg is only charged after Mn/Ti and Cr, preferably as the last alloying element in the aluminum melt, in order to prevent Mg from being burned off.
  • the temperature of the aluminum melt when charging Mg is preferably less than 740°C, in particular max. 730°C.
  • the temperature of the aluminum melt when charging Cr is preferably more than 740° C., in particular at least 750° C., in order to distribute Cr uniformly in the aluminum melt.
  • the aluminum melt 25 is cast into an ingot 28 by means of continuous DC casting.
  • the aluminum melt 25 is poured, for example by means of a crucible 29, into a cooled frame mold 30 open at the bottom and solidified by spraying with water 31, so that the ingot 28 results.
  • the ingot 28 is subjected to an ingot homogenization and/or ingot preheating in a homogenization furnace 34 and in the subsequent step 36, for example, in a reversing hot rolling mill 38, it is hot-rolled to form the hot strip 40, preferably at a temperature in the range from 280° C. to 550° C. in particular a hot strip temperature of 280°C to 350°C being set. Due to the low Na content of the aluminum alloy of the ingot 28, despite the high Mg content, there are no edge cracks during hot rolling.
  • the hot strip 40 is cold-rolled in several passes without intermediate annealing on one or more cold-rolling stands 44, so that finally a cold strip 46 with a final thickness in the range of 1 to 3 mm results.
  • the overall degree of rolling is at least 70% during cold rolling, with the degree of rolling in the last rolling pass being less than 33%.
  • the cold strip 46 is guided through a straightening system 50 with a plurality of straightening rollers 52 arranged offset relative to one another and straightened as a result.
  • the straightening rollers 52 each have a diameter of ⁇ 60 mm, so that the formation of surface defects during straightening is avoided.
  • the cold strip 46 is cut directly into sheets 56 by means of a cutting device 54 without being rolled up into a coil in the meantime. This in turn avoids one-sided compression or expansion of the cold strip 46 .
  • Aluminum sheets 56 produced by the method described above are particularly well suited for further use in a superplastic forming process.
  • FIG. 1 shows an exemplary embodiment for using one with the method from FIG 1 produced aluminum sheet 56 for the production of a component 66 by means of superplastic forming.
  • the aluminum sheet 56 is heated to a temperature in the range from 450°C to 520°C.
  • the heating can e.g. as in 2 shown as an example in a chamber furnace or a continuous furnace 70 .
  • the aluminum sheet 56 can also be heated directly in a forming tool 78 for forming the aluminum sheet 56 .
  • a separate furnace 70 can be dispensed with.
  • step 42 out 1 Due to the high dislocation density introduced into the material, when the aluminum sheet 56 is heated, for example in the furnace 70 or in the tool 78, spontaneous recrystallization of the aluminum sheet 56 occurs, with the formation of a very fine structure, the has an advantageous effect on the subsequent superplastic forming. Compared to a chamber furnace, heating in the tool or in the continuous furnace in particular favors superplastic forming, since the transfer and dwell times, during which the material is exposed to high (forming) temperatures, are minimized and grain growth before the actual forming is further minimized.
  • a second step 72 the aluminum sheet 56 is arranged between a first die half 74 and a second die half 76 of the forming tool 78 for superplastic forming, unless this has already happened beforehand for heating the aluminum sheet 56 in the forming tool 78.
  • the first die half 74 has 2 exemplarily an indentation 80 and the second die half 76 a corresponding bulge 82 .
  • the two die halves 74, 76 can also have more complex contours for producing a component with a complex shape.
  • the two die halves 74, 76 are moved together, with the aluminum sheet 56 being formed superplastically.
  • the degree of deformation of the aluminum sheet 56 is locally 100% or more in some cases. Because of the good properties of the aluminum sheet 56 for superplastic forming, in particular the fine and uniform microstructure, the aluminum sheet 56 does not constrict or tear despite the high degree of forming.
  • the forming tool 78 can therefore Step 86 a damage-free finished component 66 can be removed.
  • the component 66 produced in this way also has a high surface quality without noticeable surface defects.
  • the properties of the aluminum sheet 56 allow superplastic forming to be performed very quickly.
  • the two die halves 74, 76 can be brought together within a few minutes, preferably in a maximum of 5 minutes. The production time of the component 66 can thus be shortened and the cycle rate of the forming processes can be increased.
  • figure 3 shows a further exemplary embodiment for the use of a device according to the method 1 manufactured aluminum sheet 56 'by superplastic forming.
  • heating in the tool or in a continuous furnace favors superplastic forming, since the transfer and dwell times, during which the material is exposed to high (forming) temperatures, are minimized and grain growth before the actual forming is further minimized .
  • step 92 the aluminum sheet 56' is positioned between a first mold half 94 and a second mold half 96 of the forming tool 98 for blow forming, unless the aluminum sheet 56' has already been placed there for heating in the forming tool 98 beforehand.
  • the first tool half 94 has, for example, an indentation 100 corresponding to the target shape of the component to be produced.
  • the illustrated shape of the first tool half 94 is only an example and can be considerably more complex in practice.
  • a channel 102 for blowing in a gas is provided in the second tool half 96 .
  • the first and second tool halves 94, 96 are moved together and a gas 106 is applied at a pressure of, for example, 2 bar blown through the channel 102 in the area of the indentation 100 against the aluminum sheet 56 ′, so that the aluminum sheet 56 ′ is superplastically formed until it rests against the contour of the indentation 100 .
  • the degree of deformation of the aluminum sheet 56' is locally 100% or more in some cases.
  • the aluminum sheet 56' does not constrict or tear despite the high degree of forming.
  • a damage-free, finished component 110 can therefore be removed from the forming tool 98 in the last step 108.
  • the component 110 produced in this way also has a high surface quality without noticeable surface defects.
  • the properties of the aluminum sheet 56' allow superplastic forming to be performed very quickly.
  • the gas 106 can be introduced through the channel 102 with such a pressure that the aluminum sheet 56' molds itself to the contour of the indentation 100 within a few minutes, preferably within a maximum of 5 minutes.
  • the production time of the component 110 can thus be shortened and the cycle rate of the forming processes can be increased.
  • an aluminum melt A with the composition given in Table 1 was first produced by melting primary aluminum in an aluminum melting furnace and at the same time with additives to achieve this the desired Mn, Mg and er contents. Furthermore, an aluminum melt B with the same composition was produced, with Mn and Cr being charged separately, ie the Cr-containing additives to achieve the desired Cr content were only added after setting the desired Mn content and subsequent homogenization of the aluminum melt by stirring. As a result, the Cr content in the preliminary aluminum melt was less than 0.05% by weight during the adjustment of the desired Mn content and during the subsequent homogenization of the melt and was only then adjusted to the target value.
  • Ingots were cast from the two aluminum melts A and B, which were produced in different ways, and strips were produced by hot and cold rolling.
  • the bands showed coarse particles both on the surface and in their interior, the composition of which was analyzed using WDX analysis (wavelength-dispersive X-ray spectroscopy).
  • Table 2 shows the results of WDX analysis on six different coarse particles (Nos. 1-6) of a strip from Molten Aluminum A, of which particles Nos. 1-4 are on the surface and particles 5 and 6 are on the inside of the band were arranged: ⁇ b>Table 2 ⁇ /b> Particle No.
  • the numbers given in Table 2 are pulse numbers from the WDX analysis for the respective elements. The numbers are roughly proportional to the content of the elements in each particle.
  • the strips from aluminum melt B showed practically no coarse particles or phases, i.e. only very fine, but practically no coarse Al(Mn,Fe,Cr)Si phases formed due to the separate charging of Mn and Cr in the melt .
  • the tested alloy with the composition from Table 1 has a lower Mg content than is provided according to the present teaching.
  • the separate charging of Ti has also turned out to be advantageous in order to prevent the formation of coarse phases.
  • an aluminum melt C was produced with the composition listed in Table 3 below, with (as in the aluminum melt B described above) Mn and Cr being charged separately from one another with intermediate homogenization of the melt.
  • the aluminum melt C was cast into an ingot by DC continuous casting.
  • the ingot was preheated and a cold strip having a thickness of 1.5 mm was produced by subsequent hot and cold rolling without intermediate annealing, with a total cold rolling thickness reduction of 75%.
  • the cold strip was then straightened using straightening rolls, each with a diameter of more than 60 mm, and cut into sheets.
  • figure 5 shows a picture of a polished and barked section of one of the sheets in the as-rolled H19 condition, ie before the heat treatment. The grains, elongated by rolling, are clearly visible.
  • FIG. 12 shows an image of a polished and barked section of a sheet heat treated at 450°C for 1 minute.
  • the fine-grained structure with grain sizes between 5 and 15 ⁇ m and an average grain diameter of 7 ⁇ m is clearly visible. This shows that the fine-grained structure, which is important for superplastic forming, is achieved almost instantaneously when the material is heated to the temperature for superplastic forming (typically 450°C - 520°C).
  • 7 shows a picture of a polished and barked section of sheet metal heat treated at 450°C for 60 minutes. The structure is just as fine-grained as in 6 with an average grain diameter of also 7 ⁇ m.
  • the metallographic investigations show that the sheets do not have any coarse particles that would lead to the formation of pores during superplastic forming. This is achieved in particular through the low contents of Fe and Si and through the separate charging of Cr.
  • the micrographs in the 6 and 7 show that the sheets form a fine-grained structure at the forming temperature, which has a very stable average grain diameter even at the high forming temperatures.
  • the previously mentioned strain rate sequence was run through for a first sheet metal sample at a forming temperature of 450 °C, for a second sheet metal sample at a forming temperature of 475 °C, etc.
  • the strain rate was 5 ⁇ 10 -4 s -1 in the above strain rate sequence used a total of three times to record any hardening or softening caused by high-temperature forming.
  • the results of the forming tests are shown in the diagram in 8 in which the forming temperature T of the superplastic forming in °C is plotted on the abscissa axis and the (dimensionless) strain rate sensitivity m is plotted on the ordinate axis.
  • the values of the function m ( ⁇ ) determined as described above for the strain rates 1 ⁇ 10 -4 s -1 (+ symbols), 1 ⁇ 10 -3 s -1 (x symbols), 1 ⁇ 20 - 2 s -1 (o symbols) and 1 ⁇ 10 -1 s -1 (square symbols) are plotted.
  • the drawn lines connect the m-values of the four forming tests, each of which was determined for the same strain rate.
  • sheets produced from aluminum melt C were superplastically formed as described above at a forming temperature of 515 °C using an ISO 20032:2007-compliant testing device in a uniaxial tensile test, with the sample geometry conforming to the aforementioned standard (ISO 20032:2007 sample form S-Type).
  • the strain rate was 2.5 ⁇ 10 -4 s -1 and the total strain ⁇ at the end of the forming was 100%.
  • tensile tests were carried out on some of the sheets to determine the yield point R p0.2 and the tensile strength R m according to DIN EN ISO 6892-1:2017, with the test being carried out transversely to the rolling direction.
  • the tensile tests were carried out after the sheets had been heated in order to achieve the desired microstructure for superplastic deformation. The sheets were not superplastically deformed before the tensile tests.
  • the results of the tensile tests are shown in the diagrams in Figures 9 and 10 shown, in which the superplastic forming temperature T in °C is plotted on the abscissa axis and the yield strength R p 0.2 or the tensile strength R m is plotted on the ordinate axis, each in MPa.
  • the sheets had a yield strength R p0.2 of more than 160 MPa over the entire forming temperature range examined and even a yield strength R p0.2 of more than 170 MPa at a forming temperature of 500°C.
  • the tensile strength of the sheets was well above 310 MPa, even above 320 MPa, over the entire forming temperature range investigated.
  • the good mechanical properties after superplastic forming result in particular from the advantageous Mn content of at least 0.7% by weight, the advantageous Mg content of at least 5.2% by weight and from the separate charging of Cr and Mn.

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Claims (14)

  1. Procédé de fabrication d'un produit plat en aluminium (46 ; 56, 56'), en particulier d'un produit plat en aluminium superplastique,
    - dans lequel on prépare une masse fondue d'aluminium (25) à partir d'un alliage d'aluminium, ledit alliage d'aluminium ayant la composition suivante : 0,03 % en poids ≤ Si ≤ 0,10 % en poids, Fe ≤ 0,4 % en poids, Cu ≤ 0,1 % en poids, 0,5 % en poids ≤ Mn ≤ 1,0 % en poids, 5,2 % en poids ≤ Mg ≤ 5,5 % en poids 0,05 % en poids ≤ Cr ≤ 0,25 % en poids, Zn ≤ 0,25 % en poids, Ti ≤ 0,20 % en poids, Na ≤ 2 ppm,
    impuretés inévitables individuellement ≤ 0,05 % en poids, au total ≤ 0,15 % en poids, le reste étant de l'aluminium,
    - dans lequel l'aluminium en fusion (25) est coulé en un lingot (28),
    - dans lequel le lingot (28) est laminé à chaud pour former une bande à chaud (40),
    - dans lequel la bands à chaud (40) est laminé à froid pour former une bande à froid (46) et
    - dans lequel la bande à froid (46) est redressé.
  2. Procédé selon la revendication 1,
    caractérisé en ce que l'alliage d'aluminium présente une teneur en Fe de 0,05 à 0,15 % en poids et/ou une teneur en Cu de 0,05 % en poids au maximum.
  3. Procédé selon la revendication 1 ou 2,
    caractérisé en ce que l'alliage d'aluminium présente une teneur en Mn de 0,7 % en poids à 1,0 % en poids.
  4. Procédé selon l'une quelconque des revendications 1 à 3,
    caractérisé en ce que l'alliage d'aluminium présente une teneur en Zn de 0,06 % en poids maximum et/ou une teneur en Ti dans la plage de 0,015 à 0,03 % en poids.
  5. Procédé selon l'une quelconque des revendications 1 à 4,
    caractérisé en ce que l'alliage d'aluminium présente une teneur en B de 50 ppm maximum et/ou une teneur en Ca de 15 ppm maximum et/ou une teneur en Li de 15 ppm maximum.
  6. Procédé selon l'une quelconque des revendications 1 à 5,
    caractérisé en ce que la masse fondue d'aluminium (25) est préparée en fondant ensemble une masse fondue d'aluminium préliminaire (10) avec des additifs pour obtenir la composition de la masse fondue d'aluminium (25) à préparer, au moins deux des éléments d'alliage Cr, Mn et Ti, de préférence les trois éléments d'alliage Cr, Mn et Ti, étant chargés séparément.
  7. Procédé selon l'une quelconque des revendications 1 à 6,
    caractérisé en ce que le taux de laminage lors du laminage à froid est globalement compris entre 70% et 80%, le taux de laminage lors de la dernière passe étant de préférence inférieur à 33%.
  8. Procédé selon l'une quelconque des revendications 1 à 7,
    caractérisé en ce que la bande à froid (46) est découpé en tôles (56, 56') après le redressage, sans enroulement intermédiaire.
  9. Procédé selon l'une quelconque des revendications 1 à 8,
    caractérisé en ce que le redressage de la bande à froid (56) est effectué au moyen de rouleaux de dressage (52) ayant un diamètre supérieur à 60mm.
  10. Produit plat en aluminium (46; 56, 56'), en particulier produit plat en aluminium superplastique, fabriqué par un procédé selon l'une quelconque des revendications 1 à 9.
  11. Produit plat en aluminium selon la revendication 10,
    caractérisé en ce que le produit plat en aluminium présente, après un traitement thermique pendant 30 minutes à 500 °C, une limite d'élasticité Rp0,2 d'au moins 160 MPa, en particulier d'au moins 170 MPa, et une résistance à la traction Rm d'au moins 310 MPa, en particulier d'au moins 320 MPa.
  12. Produit plat en aluminium selon la revendication 10 ou 11,
    caractérisé en ce que le produit plat en aluminium présente une porosité inférieure à 1,5 %, en particulier inférieure à 1 %, après un formage superplastique à une température de formage de 515°C, un taux d'allongement de 2,5×10-4 s-1 et un allongement total de 100 %.
  13. Utilisation d'un produit plat en aluminium (46; 56, 56') selon l'une des revendications 10 à 12 pour la fabrication d'un produit en aluminium (66, 110) par formage superplastique du produit plat en aluminium (46; 56, 56'), en particulier par soufflage.
  14. Utilisation selon la revendication 13,
    caractérisée en ce que le formage superplastique est effectué avec un taux d'allongement d'au moins 10-3 s-1, en particulier d'au moins 10-2 s-1.
EP19701587.8A 2018-01-16 2019-01-15 Alliage d'aluminium, méthode de fabrication d'un produit plat d'aluminium, le produit plat d'aluminium et utilisation Active EP3740598B1 (fr)

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EP18151840.8A EP3511433A1 (fr) 2018-01-16 2018-01-16 Alliage d'aluminium, méthode de fabrication d'un produit plat d'aluminium, le produit plat d'aluminium et utilisation
PCT/EP2019/050899 WO2019141666A1 (fr) 2018-01-16 2019-01-15 Alliage d'aluminium, procédé de fabrication d'un produit plat en aluminium, produit plat en aluminium et son application

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JPS59159961A (ja) * 1983-02-28 1984-09-10 Mitsubishi Alum Co Ltd 超塑性Ａｌ合金
JP2640993B2 (ja) * 1990-06-11 1997-08-13 スカイアルミニウム株式会社 超塑性成形用アルミニウム合金圧延板
JP2860074B2 (ja) * 1995-11-09 1999-02-24 株式会社神戸製鋼所 ミグ溶接用アルミニウム合金ワイヤ
JP3321113B2 (ja) * 1999-05-06 2002-09-03 株式会社神戸製鋼所 アルミニウム又はアルミニウム合金用ミグ溶接ワイヤ
JP4719456B2 (ja) * 2004-08-03 2011-07-06 古河スカイ株式会社 高温ブロー成形用アルミニウム合金板

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LAVENDER C A ET AL: "Development of superplasticity in 5083 aluminum with additions of Mn and Zr", vol. 170/172, no. PNL-SA-23032; CONF-9405193-3, 1 May 1994 (1994-05-01), pages 279 - 286, XP009517481, ISBN: 978-0-87849-685-3, Retrieved from the Internet <URL:https://www.osti.gov/biblio/10177422-development-superplasticity-aluminum-additions-mn-zr> DOI: 10.4028/WWW.SCIENTIFIC.NET/MSF.170-172.279 *
YANG H S ET AL: "On the fabrication aspect of commercial superplastic 5083 aluminum alloy sheets", no. CONF-950201, 31 December 1995 (1995-12-31), pages 17 - 24, XP009517482, ISBN: 978-0-87339-300-3, Retrieved from the Internet <URL:https://www.osti.gov/biblio/194181-fabrication-aspect-commercial-superplastic-aluminum-alloy-sheets> *

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US20200325560A1 (en) 2020-10-15
EP3511433A1 (fr) 2019-07-17
EP3740598A1 (fr) 2020-11-25
EP3740598C0 (fr) 2023-06-28
WO2019141666A1 (fr) 2019-07-25

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