EP2888383A1 - Bande d'almg à fort pouvoir de déformation, résistante à la corrosion intercristalline - Google Patents

Bande d'almg à fort pouvoir de déformation, résistante à la corrosion intercristalline

Info

Publication number
EP2888383A1
EP2888383A1 EP13756053.8A EP13756053A EP2888383A1 EP 2888383 A1 EP2888383 A1 EP 2888383A1 EP 13756053 A EP13756053 A EP 13756053A EP 2888383 A1 EP2888383 A1 EP 2888383A1
Authority
EP
European Patent Office
Prior art keywords
aluminum alloy
alloy strip
weight
strip
annealing
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP13756053.8A
Other languages
German (de)
English (en)
Other versions
EP2888383B1 (fr
Inventor
Henk-Jan Brinkman
Olaf Engler
Natalie Hörster
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Speira GmbH
Original Assignee
Hydro Aluminium Rolled Products GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
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Application filed by Hydro Aluminium Rolled Products GmbH filed Critical Hydro Aluminium Rolled Products GmbH
Priority to EP13756053.8A priority Critical patent/EP2888383B1/fr
Publication of EP2888383A1 publication Critical patent/EP2888383A1/fr
Application granted granted Critical
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Revoked legal-status Critical Current
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Links

Classifications

    • 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • 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
    • 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
    • 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
    • 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

Definitions

  • the invention relates to a cold-rolled aluminum alloy strip consisting of an AlMg-aluminum alloy and a process for its preparation. Furthermore, even corresponding components are made from the
  • Aluminum magnesium (AlMg) alloys of type AA 5xxx are used in the form of sheets or plates or strips for the construction of welded or joined structures in shipbuilding, automotive and aircraft construction. They are characterized in particular by a high strength, which increases with increasing
  • ⁇ -A15Mg3 phases separate out along the grain boundaries, which are called ⁇ -particles and can be selectively dissolved in the presence of a corrosive medium. As a result, especially the very good
  • Aluminum alloy of type AA 5182 (AI 4.5% Mg 0.4% Mnj not in
  • heat-stressed areas is used, provided that the presence of a corrosive medium, such as water in the form of moisture, must be expected.
  • a corrosive medium such as water in the form of moisture
  • NAMLT test Standard test according to ASTM G67, in which the samples are exposed to nitric acid and the mass loss due to the
  • Corrosion are more than 15 mg / cm 2 .
  • Automotive sheets require very good formability, as in the case of interior door parts, for example.
  • the requirements are essentially determined by the rigidity of the respective component, where the strength of the material plays only a minor role.
  • the components often go through multi-stage
  • Aluminum alloy has a great influence on the possibilities of using these materials.
  • the previously known materials have meant that the side walls of a motor vehicle could not be pulled deep from a single sheet, which not only a redesign of the side wall, but also additional process steps to provide the side wall part of a
  • the forming behavior can, for example, in stretch-stretching by a
  • Camber test according to Erichsen (DIN EN ISO 20482) are measured, in which a test piece is pressed against the sheet, so that it comes to a cold deformation. During cold working, the force as well as the punch away from the specimen is measured until there is a load drop which causes the formation of a crack.
  • the SZ32 stretch drawing measurements mentioned in the application were made with a punch head diameter of 32 mm and a
  • thermoformability Diameter of 35.4 mm with the help of a Teflon drawing film to reduce friction performed. Further measurements of the thermoformability were made by the so-called plane-strain-depression experiment with a Nakajima Geometry according to DIN EN ISO 12004 with a punch diameter of 100 mm. These are samples with a specified geometry
  • Aluminum alloy layers have the disadvantages that the production is complex and also at joints where the aluminum composite is connected to other parts, for example, cut edges, holes and breakthroughs continue to be given an increased risk of corrosion.
  • the present invention therefore deals with single-layered
  • the object of the present invention is to provide a single-layered aluminum alloy strip which has sufficient resistance to intergranular corrosion and is nevertheless very easy to form, so that deep-drawn parts of large dimensions, for example door parts of motor vehicles, can be provided with sufficient strength ,
  • a method is to be specified with which single-layer aluminum alloy strips can be produced.
  • components produced from the aluminum alloy strips according to the invention are to be specified.
  • the object is achieved by a cold-rolled aluminum alloy strip consisting of an AlMg aluminum alloy, the aluminum alloy comprising the following
  • Alloy components comprising:
  • the final soft annealing of the aluminum alloy strip has been carried out in a continuous furnace.
  • Aluminum alloy of the aluminum alloy strip make it possible to achieve degrees of deformation, which allow sufficient strength, the production of large-scale, deep-drawn aluminum sheet metal parts.
  • Aluminum alloy in addition to one or more of the following alloy contents content limits: 0.03 wt% Si ⁇ 0.10 wt%,
  • the limited alloying content of copper to at most 0.1% by weight leads to an improvement in the corrosion resistance of the aluminum alloy strip.
  • a Cu content of 0.04 wt .-% to 0.08 wt .-% is achieved that copper participates in an increase in strength, but still does not reduce the corrosion resistance too strong.
  • Titanium is commonly used in continuous casting of the aluminum alloy
  • Grain refining agent added for example, in the form of Ti-boride wire or rods. Therefore, the aluminum alloy in another
  • Embodiment a Ti-content of at least 0.01 wt .-% on.
  • a further improvement of the corrosion behavior and the formability of the aluminum alloy strip can be achieved in that the
  • Aluminum alloy additionally has one or more of the following restrictions on the contents of alloy constituents:
  • Al uminiumleg istsbandes influenced and thus in the lowest possible proportions in the aluminum alloy of the aluminum alloy strip according to the invention may be included.
  • the zinc content is set below the impurity threshold of 0.05% by weight to reduce the overall corrosion behavior of the
  • Aluminum alloy strip not to deteriorate.
  • Type AA5182 aluminum alloy values in conjunction with the silicon and manganese levels as described above have an effect on the
  • Formability has. Iron, in combination with silicon and manganese, contributes to the performance of the aluminum alloy strip so that, preferably, the Fe content of the aluminum alloy strip is 0.1 wt.% To 0.25 wt. 10 wt .-% to 0.20 wt .-% is.
  • the Mn content according to a further embodiment of the aluminum alloy strip which should preferably be limited to 0.20 wt .-% to 0.30 wt .-%, in order to optimize the formability of
  • Aluminum alloy ribbon having a Mg content of 4.2 wt .-% to 4.4 wt .-% can be achieved.
  • the aluminum alloy strip according to a next embodiment has a thickness of 0.5 mm to 4 mm.
  • the thickness is 1 mm to 2.5 mm, as in this area are the most applications of the aluminum alloy strip.
  • Aluminum alloy strip in the soft state a yield strength R p o, 2 of min. 110 MPa and a tensile strength R m of min. 255 MPa. It has
  • aluminum alloy tapes with appropriate yield strengths and tensile strengths are particularly well suited for use in the
  • the above-described object is achieved by a method for producing an aluminum alloy strip according to the above-described embodiments in that the method comprises the following method steps:
  • Homogenizing the rolling billet ensures a homogenous structure and a homogeneous distribution of the alloy components in the hot rolling billet to be rolled. Hot rolling at temperatures of 280 ° C - 500 ° C allows a
  • the final cold rolling step is limited to a degree of rolling of 40% to 70% or 50% to 60%, to provide in both cases in the soft annealing for a continuous recrystallization of the aluminum alloy strip.
  • the soft annealing of the finished rolled aluminum alloy strip takes place in the continuous furnace, which usually heating rates of 1 - 10 ° C / sec. and thus, in contrast to chamber furnaces, in which an entire coil is heated, due to the rapid heating have a significant influence on the subsequent properties of the structure of the aluminum alloy strip.
  • the continuous furnace usually heating rates of 1 - 10 ° C / sec. and thus, in contrast to chamber furnaces, in which an entire coil is heated, due to the rapid heating have a significant influence on the subsequent properties of the structure of the aluminum alloy strip.
  • improved formability of the strip is achieved in comparison to variants annealed in the chamber furnace.
  • Aluminum alloy strip can also be produced with an intermediate annealing.
  • the intermediate annealing of the aluminum alloy strip can take place both in the chamber furnace and in the continuous furnace. An influence on the formability could not be determined.
  • the decisive factor is which degree of rolling is achieved during cold rolling to final thickness and whether the soft annealing of the strip takes place in the continuous furnace.
  • the formability and the corrosion resistance are determined in connection with the alloy composition.
  • the aluminum alloy strip according to a further embodiment of the method after annealing to a temperature of max. 100 ° C, preferably to max. Cooled to 70 ° C and then
  • the intermediate annealing can be carried out in a batch furnace or in a continuous furnace. If the aluminum alloy strip cold rolled to a final thickness of 0.5 mm - 4 mm, preferably to a final thickness of 1 mm - 2.5 mm, the typical application areas, especially in automotive very well convertible sheets are available, which can be deep-drawn extensively and simultaneously high strength combined with sufficient
  • the soft annealing is carried out in a continuous furnace at a metal temperature of 350 ° C - 550 ° C, preferably at 400 ° C - 450 ° C for 10 sec. - 5 min., Preferably 20 sec - 1 min. This ensures that the cold strip recrystallized sufficiently by and the corresponding properties in relation to the very good formability and the average grain size with high process reliability and
  • the object shown above is achieved by a component for a motor vehicle which has been produced from the aluminum alloy strip according to the invention.
  • the components are characterized by the fact that they, as already stated, can be deep-drawn over a large area and thus, for example, large-area components can be made available for the automotive industry. In addition, these have due to the provided strength and the necessary
  • the component is according to a further embodiment, a body part or a body part of a motor vehicle, which is loaded in addition to high strength requirements and temperature.
  • the "body-in-white parts" for example, a door inner part or a
  • Tailgate inner part made from the aluminum alloy strip according to the invention.
  • Fig. 1 is a schematic flow diagram of an embodiment of the
  • 2a is a plan view of the sample geometry for the tarpaulin strain measurement according to DIN EN ISO 12004,
  • Fig. 4 shows a typical embodiment of a large, deep-related
  • Fig. 1 shows the sequence of embodiments for the production of
  • FIG. 1 shows schematically the various process steps of the manufacturing process of the aluminum alloy strip according to the invention.
  • step 1 a billet of an AlMg aluminum alloy is cast with the following alloying constituents, for example in DC continuous casting:
  • the rolling ingot in procedural step 2 is subjected to homogenization, which can be carried out in one or more stages.
  • a homogenization temperatures of the rolling ingot are reached from 480 to 550 ° C for at least 0.5 h.
  • process step 3 the rolling ingot is then hot rolled, with typical temperatures of 280 ° C to 500 ° C can be achieved.
  • the final thicknesses of the hot strip are, for example, 2.8 to 8 mm.
  • Hot strip thickness can be selected so that after hot rolling only a cold rolling step 4 takes place, in which the hot strip with a rolling degree of 40% to 70%, preferably 50% to 60% in its thickness is reduced to the final thickness.
  • the aluminum alloy strip cold rolled to final thickness is subjected to soft annealing.
  • the soft annealing is carried out according to the invention in a continuous furnace.
  • the second way was used with an intermediate glow.
  • the hot strip after hot rolling according to process step 3 is fed to a cold rolling 4a, which cold rolled the aluminum alloy strip to an intermediate thickness, which is determined such that the final cold rolling degree of final thickness 40% to 70% or 50% to 60%.
  • the aluminum alloy ribbon is preferably recrystallized throughout.
  • Intermediate annealing was carried out in the embodiments either in a continuous furnace at 400 ° C to 450 ° C or in the chamber furnace at 330 ° C to 380 ° C.
  • the intermediate annealing is shown in FIG. 1 with method step 4b. in the
  • Process step 4c of FIG. 1 is the intermediate annealed
  • step 4c aluminum alloy strip is fed to a cold rolling to final thickness, wherein the degree of rolling in step 4c is between 40% and 70%, preferably between 50% and 60%. Subsequently, the aluminum alloy ribbon is returned to the soft state by a soft annealing, wherein the
  • Soft annealing is carried out according to the invention in a continuous furnace at 400 ° C to 450 ° C.
  • the anneals of Comparative Examples in Table 4 were carried out in the chamber furnace (KO) at 330 ° C to 380 ° C.
  • different degrees of rolling were set after intermediate annealing in addition to different aluminum alloys.
  • the values for the degree of rolling after the intermediate annealing are also given in Tables 1 and 4.
  • the mean grain diameter of the soft-annealed aluminum alloy strip was determined. For this purpose, longitudinal slices were anodized according to the Barker method and then measured under the microscope in accordance with ASTM E1382 and the mean grain size determined by the mean grain diameter.
  • mechanical properties in particular the yield strength R p o, 2, tensile strength R m , the uniform elongation A g and the elongation Aeomm determined, Table 2, 5.
  • mechanical characteristics of the aluminum alloy strips are also the mean particle sizes according to ASTM E1382 in ⁇ indicated.
  • corrosion resistance was against Intercrystalline corrosion measured according to ASTM G67, without additional heat treatment in the initial state (output Oh).
  • a first heat treatment consisted of storing the aluminum strips for 20 minutes at 185 ° C to image the KTL cycle.
  • the aluminum alloy strips were additionally stored for 200 hours or 500 hours at 80 ° C. and then subjected to the corrosion test. Since transformations of aluminum alloy strips or sheets can additionally affect the corrosion resistance, the
  • Aluminum alloy tapes were stretched by about 15% in a further test, subjected to a heat treatment or storage at elevated temperature, and then subjected to an intergranular corrosion test according to ASTM G67 in which mass loss was measured.
  • variant 2 had a mean particle size of 18 ⁇ compared to 33 ⁇ variant 1 had.
  • the tapes in Table 1 were brought to a temperature of 400 ° C - 450 ° C in a continuous belt oven for 20 sec. - 1 min., Then cooled and wound up at less than 100 ° C. The samples taken were then measured according to the corresponding DIN EN ISO standards as indicated in Table 2. It can be seen from Table 2 that variant 1 does not reach the value of 110 MPa with respect to the yield strength and that it does not reach the diagonal measurement,
  • variant 2 also reached the yield strength values of at least 110 M Pa in all tensile directions. It can be clearly seen that variant 3 with the highest Mg content of 4.95% by weight achieves the highest yield strength and tensile strength values. In addition, it can be seen that the varying degree of rolling between variants 1 and 2 not only significantly affects the grain size, but in particular raises the yield strength to a value of significantly more than 110 MPa.
  • the inventive alloy variant 2 has a lower anisotropy compared to the reference, which is reflected in low values of the planar anisotropy Ar.
  • the planar anisotropy Ar is defined as V2- (n + rq-2 rD), where rL, rQ and r »are the r-values in longitudinal, transverse and
  • Diagonal direction correspond.
  • the mean r-value f calculated from l / 4- (rL + rQ + 2ro), does not differ significantly from that of the reference material.
  • Table 3 now shows the measured values taken with respect to intergranular corrosion resistance. It has been found that variant 2 according to the invention has comparable values with respect to the measured values of the reference, in particular with regard to the long-term loading, both in the stretched state and in the unstretched state. Here the variant 2 and the reference are nearly identical. Variant 3, which indeed has the highest yield strength and tensile strength values, showed in the corrosion test, however, that the excessive Mg content would lead to excessive mass loss, especially in the long-term tests, which, in addition to a short tempering cycle of 20 min. At 185 ° C. In addition, a long-term load of 200 hours at 80 ° C have gone through, the result.
  • variant 2 was superior to the reference alloy in the stretch-drawing properties in the SZ32 deepening test as well as in the plane-strain creep test.
  • the significantly improved forming behavior of the aluminum alloy strip according to Variant 2 over the reference aluminum alloy strip shows that even with a reduced Mg content, equivalent yield strengths and tensile strengths can be achieved with the reference alloy without sacrificing resistance to intergranular corrosion. This was demonstrated in particular by the mass loss measurement according to ASTM G67 in the NAML test. Significantly could with the variant 2 an improvement of thermoforming behavior in
  • Camber test according to Erichsen by 7% and in Plane-Strain-Tiefungs broke be determined by about 10%, which the additional reshaping potential of
  • Aluminum alloy ribbons according to the invention shows. This additional
  • Forming potential can be used to produce deep-drawn, large-area sheet-metal shaped parts, for example, door inner parts of a car.
  • Fig. 2a the geometry of the sample body 1 is shown. From a
  • the waisted specimen 1 is cut so that the web 4 has a width of 100 mm and the radii 2 at the waistings 20 mm. With the measure 3, which is 100 mm, the punch diameter is shown.
  • Fig. 2b now shows the sample 1 clamped between two
  • Hold-downs 5, 6 The test piece 1, which was placed on a receptacle 8 and was pressed against the support via the hold-downs 5, 6, is pulled in the direction of the arrow with a punch 7, which has a hemispherical tip with a radius of 100 mm Service.
  • the hold-downs have additional
  • a Teflon drawing film was used to reduce friction in SZ32.
  • Comparative examples were prepared and measured in terms of their mechanical properties and resistance to intergranular corrosion. It has been found that the combination of the use of the continuous furnace in conjunction with a specifically selected particle size of 15 ⁇ - 30 ⁇ , preferably 15 ⁇ - 25 ⁇ leads to a good compromise between corrosion resistance and mechanical measurements.
  • the invention
  • Embodiments Nos. 3, 4, 7, 11 and 15 are equipped with a sufficient resistance to intergranular corrosion and also have the mechanical measurements R p o, 2 and R m necessary for use in the automotive sector, so that they are ideal for the provision of large-area, deep-drawn components are suitable.
  • Aluminum alloy strip of the present invention can be made from a single, deep-drawn sheet metal. The sheet thickness is thereby

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)
  • Conductive Materials (AREA)

Abstract

L'invention concerne une bande d'alliage d'aluminium laminée à froid composée d'un alliage d'aluminium AlMg, ainsi qu'un procédé pour sa fabrication. L'invention concerne également des éléments correspondants fabriqués à partir des bandes d'alliage d'aluminium. L'invention vise par ailleurs à mettre en oeuvre une bande d'alliage d'aluminium monocouche présentant une résistance suffisante à la corrosion intercristalline et pouvant toutefois être déformée aisément, de telle manière qu'il est possible de fabriquer des pièces à emboutissage profond, même de grandes tailles, par exemple des parties intérieures de portières de véhicules à moteur. A cet effet, on emploie une bande d'alliage d'aluminium composée d'un alliage d'aluminium AlMg présentant les constituants suivants : Si ≤ 0,2 % en poids, Fe ≤ 0,35 % en poids, Cu ≤ 0,15 % en poids, 0,2 % en poids ≤ Mn < 0,35 % en poids, 4,1 % en poids ≤ Mg ≤ 4,5 % en poids, Cr ≤ 0,1 % en poids, Zn ≤ 0,25 % en poids, Ti ≤ 0,1 % en poids, reste d'Al et impuretés inévitables représentant individuellement au plus 0,05 % en poids, et au total au plus 0,15 % en poids, la bande d'alliage d'aluminium présentant une structure recristallisée, la taille moyenne des grains étant comprise entre 15 μm et 30 μm, de préférence entre 15 μm et 25 μm, et le recuit d'adoucissement final de la bande d'alliage d'aluminium étant réalisé dans un four continu.
EP13756053.8A 2012-08-22 2013-08-22 Bande d'alliage en aluminium résistant à la corrosion intercristalline et son procédé de fabrication Revoked EP2888383B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP13756053.8A EP2888383B1 (fr) 2012-08-22 2013-08-22 Bande d'alliage en aluminium résistant à la corrosion intercristalline et son procédé de fabrication

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
EP12181356 2012-08-22
EP2013064736 2013-07-11
EP13756053.8A EP2888383B1 (fr) 2012-08-22 2013-08-22 Bande d'alliage en aluminium résistant à la corrosion intercristalline et son procédé de fabrication
PCT/EP2013/067487 WO2014029856A1 (fr) 2012-08-22 2013-08-22 Bande d'almg à fort pouvoir de déformation, résistante à la corrosion intercristalline

Publications (2)

Publication Number Publication Date
EP2888383A1 true EP2888383A1 (fr) 2015-07-01
EP2888383B1 EP2888383B1 (fr) 2016-03-30

Family

ID=49084999

Family Applications (1)

Application Number Title Priority Date Filing Date
EP13756053.8A Revoked EP2888383B1 (fr) 2012-08-22 2013-08-22 Bande d'alliage en aluminium résistant à la corrosion intercristalline et son procédé de fabrication

Country Status (9)

Country Link
US (1) US20150159250A1 (fr)
EP (1) EP2888383B1 (fr)
JP (1) JP5923665B2 (fr)
KR (1) KR101709289B1 (fr)
CN (1) CN104937120B (fr)
CA (1) CA2882614C (fr)
ES (1) ES2569945T3 (fr)
RU (1) RU2608931C2 (fr)
WO (1) WO2014029856A1 (fr)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20160186301A1 (en) * 2013-08-21 2016-06-30 Drexel University Annealing Process
CN107810284A (zh) * 2015-06-05 2018-03-16 诺维尔里斯公司 高强度5xxx铝合金以及其制造方法
KR101911037B1 (ko) * 2015-06-25 2018-10-23 하이드로 알루미늄 롤드 프로덕츠 게엠베하 고강도이며 용이하게 성형 가능한 almg-스트립 및 그 제조 방법
WO2018158165A1 (fr) * 2017-02-28 2018-09-07 Tata Steel Ijmuiden B.V. Procédé de fabrication d'une bande d'acier comprenant une couche de revêtement en alliage d'aluminium
WO2020182506A1 (fr) 2019-03-08 2020-09-17 Aleris Aluminum Duffel Bvba Procédé de fabrication d'un produit de tôle de série 5xxx
CN113186413A (zh) * 2021-04-29 2021-07-30 郑州明泰实业有限公司 一种新能源汽车用5083-o态电池壳侧板的制备方法
WO2023031334A1 (fr) 2021-09-03 2023-03-09 Speira Gmbh Bande d'alliage d'aluminium optimisée pour le formage, et son procédé de fabrication

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4151013A (en) 1975-10-22 1979-04-24 Reynolds Metals Company Aluminum-magnesium alloys sheet exhibiting improved properties for forming and method aspects of producing such sheet
JP2671121B2 (ja) 1986-03-10 1997-10-29 スカイアルミニウム 株式会社 伸び、曲げ性、張出し性に優れた成形加工用アルミニウム合金圧延板およびその製造方法
JPH0668146B2 (ja) 1986-09-09 1994-08-31 スカイアルミニウム株式会社 アルミニウム合金圧延板の製造方法
EP0681034A1 (fr) 1994-05-06 1995-11-08 The Furukawa Electric Co., Ltd. Procédé de fabrication d'une feuille en alliage d'aluminium pour carrosserie de véhicules et feuille en alliage ainsi obtenue
FR2740144B1 (fr) 1995-10-18 1997-11-21 Pechiney Rhenalu Alliage almg pour constructions soudees a caracteristiques mecaniques ameliorees
NL1003453C2 (nl) 1996-06-28 1998-01-07 Hoogovens Aluminium Nv Aluminiumplaat van het AA5000-type en een werkwijze voor het vervaardigen daarvan.
WO1998040528A1 (fr) * 1997-03-07 1998-09-17 Alcan International Limited Procede de production de tole aluminiee
DE10231437B4 (de) * 2001-08-10 2019-08-22 Corus Aluminium N.V. Verfahren zur Herstellung eines Aluminiumknetlegierungsprodukts
RU2230131C1 (ru) * 2002-09-20 2004-06-10 Региональный общественный фонд содействия защите интеллектуальной собственности Сплав системы алюминий-магний-марганец и изделие из этого сплава
ATE370256T1 (de) * 2003-04-08 2007-09-15 Hydro Aluminium Deutschland Flächiges, gewalztes halbzeug aus einer aluminiumlegierung
JP4534573B2 (ja) * 2004-04-23 2010-09-01 日本軽金属株式会社 高温高速成形性に優れたＡｌ‐Ｍｇ合金板およびその製造方法
RU2280705C2 (ru) * 2004-09-15 2006-07-27 Открытое акционерное общество "Каменск-Уральский металлургический завод" Сплав на основе алюминия и изделие из него
EP1852251A1 (fr) * 2006-05-02 2007-11-07 Aleris Aluminum Duffel BVBA Matériel de tole d'aluminium composite
JP2008202134A (ja) * 2007-02-22 2008-09-04 Kobe Steel Ltd プレス成形性に優れたアルミニウム合金熱延板
JP5432642B2 (ja) * 2009-09-03 2014-03-05 株式会社Ｕａｃｊ 缶エンド用アルミニウム合金板及びその製造方法。
EP2302087B1 (fr) * 2009-09-15 2012-07-25 Hydro Aluminium Deutschland GmbH Pièces de roulement en matière active composite AL

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2014029856A1 *

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ES2569945T3 (es) 2016-05-13
CA2882614A1 (fr) 2014-02-27
WO2014029856A1 (fr) 2014-02-27
RU2608931C2 (ru) 2017-01-26
KR101709289B1 (ko) 2017-02-22
KR20150076151A (ko) 2015-07-06
CA2882614C (fr) 2018-01-02
JP2015532679A (ja) 2015-11-12
RU2015110021A (ru) 2016-10-20
US20150159250A1 (en) 2015-06-11
CN104937120B (zh) 2017-11-17
EP2888383B1 (fr) 2016-03-30
CN104937120A (zh) 2015-09-23
JP5923665B2 (ja) 2016-05-24

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