EP3981893A1 - Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque - Google Patents

Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque Download PDF

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Publication number
EP3981893A1
EP3981893A1 EP20200645.8A EP20200645A EP3981893A1 EP 3981893 A1 EP3981893 A1 EP 3981893A1 EP 20200645 A EP20200645 A EP 20200645A EP 3981893 A1 EP3981893 A1 EP 3981893A1
Authority
EP
European Patent Office
Prior art keywords
plate
weight
aluminum alloy
temperature
particles
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.)
Withdrawn
Application number
EP20200645.8A
Other languages
German (de)
English (en)
Inventor
Thomas Ebner
Stefan Pogatscher
Florian Schmid
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.)
Amag Rolling GmbH
Original Assignee
Amag Rolling 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
Application filed by Amag Rolling GmbH filed Critical Amag Rolling GmbH
Priority to EP20200645.8A priority Critical patent/EP3981893A1/fr
Priority to CN202180068191.3A priority patent/CN116324005A/zh
Priority to US18/248,302 priority patent/US20230372986A1/en
Priority to EP21798573.8A priority patent/EP4225959A1/fr
Priority to PCT/EP2021/077778 priority patent/WO2022074153A1/fr
Priority to JP2023519155A priority patent/JP2023544696A/ja
Publication of EP3981893A1 publication Critical patent/EP3981893A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • 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
    • 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
    • C22F1/043—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 silicon 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
    • C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/001—Aluminium or its alloys

Definitions

  • the invention relates to a rolled aluminum alloy plate and a method of manufacturing this plate.
  • the object of the invention is therefore to improve the strength, in particular the yield strength (R p0.2 ), of a plate made of an Al—Mg—Si aluminum alloy.
  • the invention solves the problem set with regard to the plate by the features of claim 1.
  • the aluminum alloy contains from 0.7 to 1.5% by weight silicon (Si), from 0.5 to 1.3% by weight magnesium (Mg), from 0.05 to 0.6% by weight manganese (Mn), from 0.1 to 0.3% by weight of zirconium (Zr), the prerequisites for increased strength, preferably in the yield point (R p0.2 ), can be created.
  • Si silicon
  • Mg magnesium
  • Mn manganese
  • Zr zirconium
  • a special structure of the plate can be adjusted - namely an essentially recovered structure, i.e. a structure with a low proportion of recrystallized grains.
  • the plate has a partially recrystallized structure with a degree of recrystallization of less than 25%, which can ensure increased strength if the non-recrystallized structure area of the structure is also in a recovered state and has an average sub-grain size in the rolling direction of less than 10 ⁇ m.
  • comparatively finely distributed intermetallic Zr-containing particles for example (Al,Si) 3 Zr or Al 3 Zr particles, form in the structure, which leads to pinning of the sub-grain boundaries for a led to a comparatively low degree of recrystallization while achieving comparatively small sub-grain sizes.
  • the yield point (R p0.2 ) of the sheet can be significantly increased.
  • the aluminum alloy can also optionally contain one or more of the elements listed below with the following content: up to 0.5% by weight copper (Cu); up to 0.7% by weight iron (Fe); up to 0.1% by weight chromium (Cr); up to 0.2% by weight titanium (Ti); up to 0.5% by weight zinc (Zn); up to 0.2% by weight of tin (Sn), up to 0.1% by weight of strontium (Sr), up to 0.2% by weight of vanadium (V), up to 0.2% by weight of molybdenum (Mo );
  • the plate is of rolled 6xxx series aluminum alloy.
  • the degree of recrystallization is preferably lower in order to achieve an increased proportion of recovered structure. This is particularly the case when the degree of recrystallization is less than 15%.
  • the degree of recrystallization is less than 5%, in order to be able to ensure a high proportion of recovered structure in the microstructure for high strength.
  • the above can be further improved when the mean sub-grain size in the rolling direction is 5 ⁇ m or less.
  • the strength of the plate can be further increased if it is in the T6 condition, for example the T651 condition.
  • the plate can have a yield point (R p0.2 ) of greater than 350 MPa, among other things.
  • the intermetallic phase of the aluminum alloy preferably has Zr-containing particles with an average particle size of at most 100 nm (nanometers), the number of Zr-containing particles being greater than or equal to 1 ⁇ 10 6 particles/mm 2 .
  • the pinning of the sub-grain boundaries can be improved, and thus the proportion of recovered and non-recrystallized structure can be further increased.
  • this can further reduce the mean sub-grain size of the recovered microstructure area, which can further increase the strength of the panel.
  • the above can be further improved when the average particle size of the Zr-containing particles is in the range of 30 nm to 100 nm. It can also prove to be advantageous if the number of Zr-containing particles is less than or equal to 100 ⁇ 10 6 particles/mm 2 . In addition, it can be advantageous if the number of Zr-containing particles is greater than or equal to 5 ⁇ 10 6 particles/mm 2 .
  • the plate can be suitable for mechanical engineering.
  • the invention solves the problem set with regard to the method by the features of claim 10.
  • a substantially recovered structure with a comparatively low degree of recrystallization and with a comparatively small sub-grain size can be reproducibly produced in comparison to other known methods.
  • a first homogenization at a first temperature in the range of 300 ° C to 400 ° C and a subsequent second homogenization is carried out at a second temperature in the range from 500° C. to 10° C. below a solidus temperature of the aluminum alloy.
  • accelerated cooling and often referred to as quenching
  • quenching can be understood to mean faster cooling than cooling at room temperature and still air (cf. Friedrich Ostermann, Aluminum Application Technology, 3rd edition, year of publication 2014: Cooling after solution annealing en).
  • the first homogenization can preferably take place with a first holding time of greater than or equal to 0.5 hours and/or up to 4 days and/or a maximum heating rate of 5 K/min.
  • the number of Zr-containing particles in the structure can thus be further increased.
  • the second homogenization preferably takes place with a second holding time of greater than or equal to 0.5 hours and/or up to 24 hours in order to further reduce concentration differences in the structure.
  • the hot rolling of the homogenized slab may be performed at a temperature lower than the solidus temperature of the aluminum alloy by 5°C to 100°C to obtain a preferred deformation structure.
  • the plate can be solution heat treated at a temperature in the range of 460°C to 580°C.
  • the plate can also be solution annealed with a holding time of 1 minute to 10 hours. In general, it is mentioned that solution annealing can achieve as complete a solution as possible of the alloying elements involved in hardening (cf. Friedrich Ostermann, Application Technology Aluminum, 3rd edition, year of publication 2014, ISBN 987-3-662-43806-0, page 175 )
  • the artificial aging can take place at room temperature and/or with a holding time of preferably up to 8 weeks. This can contribute to further simplifying the method.
  • Artificial aging can be carried out at a temperature in the range of 130°C to 210°C and/or for a holding time of 1 to 24 hours in order to further increase the strength of the plate.
  • the above can be further enhanced if the heat treatment takes the plate to the T6, particularly T651, temper.
  • rolled semi-finished products namely plates A and B, each with a plate thickness of 6 mm (millimeters) from a respective rolled aluminum alloy plate Si wt% mg wt% Cu wt% Mn wt% Fe wt% Zr wt% Solidus temperature °C A 0.90 0.61 0.07 0.40 0.32 - 594 B 1.07 0.81 0.30 0.41 0.36 0.21 578 and the remainder being aluminum and impurities unavoidable due to production, each with a maximum of 0.05% by weight and a maximum of 0.15% by weight in total.
  • a plate thickness of 4 mm to 150 mm, in particular 6 mm to 40 mm is conceivable for a plate.
  • Plate A alloy is an EN AW-6082 standard alloy. Based on this standard alloy EN AW-6082, the alloying elements Si, Mg and Cu were increased in content. In addition to changed Si, Mg, Cu contents, plate B also has a Zr content and thus represents the embodiment according to the invention.
  • the manufacturing process is 1 shown schematically, in the order mentioned, a homogenization (H) of a previously cast rolling slab Hot rolling (WW) of the homogenized rolling slab into a slab representing solution annealing (LG), natural aging (KA), cold working (R) and artificial aging (WA) of the slab.
  • the solid line after 1 Fig. 11 shows the process flow for the production of the plate A and the plate B in part. Partly because plate B is treated first after the dashed line and then further after the solid line during homogenization (H). This represents a special process improvement.
  • the panels A and B subjected to this method were examined by means of a tensile test (tensile test according to standard DIN EN 10002-1) with regard to mechanical parameters 0.2% proof stress R p0.2 , tensile strength R m , uniform elongation A g and elongation at break A.
  • Table 1 Mechanical characteristics of plates A and B in the T6 condition, namely T651 (* in the rolling direction) R p0.2 [MPa] ⁇ R p0.2 [MPa] Rm [MPa] A [%] Degree of recrystallization [%] Mean sub-grain size [ ⁇ m]* Zr-containing particles number [particles/mm 2 ] Mean size [nm] A 289 - 309 19 83.3 - - - B 362 +73 392 15 4.3 5 7.52x10 6 74
  • the two plates, the degree of recrystallization, the average sub-grain size and the number and average size of the Zr-containing particles in the structure were determined.
  • the degree of recrystallization was measured using a JEOL 7200F FEG-SEM EBSD detector using the two conditions (a) grain-averaged misorientation within a 3rd-order kernel with a 0.6 ⁇ m step of less than 0.5° and (b ) average band contrast of over 70% of the maximum measured band contrast.
  • the Zr-containing particle values of plate B were determined using a scanning transmission electron microscope (HAADF photographs at 17,000x magnification, Talos F200X G2 S-TEM).
  • panel B has significantly higher strength values R p0.2 and R m in the T651 temper than panel A.
  • R p0.2 and R m in the T651 temper
  • the strength of plate A is essentially based on precipitations, in particular on ⁇ ′′ precipitations (Si, Mg) that form during artificial aging, in combination with particles containing Fe and/or Mn, which stabilize the structure at higher temperatures.
  • the intermetallic phase of the aluminum alloy of plate B has Zr-containing particles with an average particle size of 74 nm.
  • the number of Zr-containing particles is 7.52 ⁇ 10 6 particles/mm 2 .
  • Al(Fe,Mn,Cr)Si-containing particles are found in the intermetallic phase of the aluminum alloy of plate A. These have an average particle size of 101 nm. The number of these Al(Fe,Mn,Cr)Si-containing particles is 1.2 ⁇ 10 6 particles/mm 2 . These particle values of plate A were determined using scanning electron micrographs (BSE micrographs at x10,000 magnification, JEOL 7200F FEG-SEM).
  • the particles of plate A are therefore not only significantly larger, their number is also many times smaller than is the case for the Zr-containing particles of plate B, which also have these Al(Fe,Mn,Cr)Si-containing particles having.
  • This high amount of comparatively smallest Zr-containing particles of plate B pinned sub-grain boundaries improved and can thus increase the proportion of recovered microstructure in the final state and ensure a further reduced sub-grain size.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Metal Rolling (AREA)
  • Conductive Materials (AREA)
EP20200645.8A 2020-10-07 2020-10-07 Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque Withdrawn EP3981893A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
EP20200645.8A EP3981893A1 (fr) 2020-10-07 2020-10-07 Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque
CN202180068191.3A CN116324005A (zh) 2020-10-07 2021-10-07 由轧制铝合金制成的板材以及用于制造该板材的方法
US18/248,302 US20230372986A1 (en) 2020-10-07 2021-10-07 Plate made of a rolled aluminum alloy and a method for producing said plate
EP21798573.8A EP4225959A1 (fr) 2020-10-07 2021-10-07 Plaque en alliage d'aluminium laminé et procédé de fabrication de ladite plaque
PCT/EP2021/077778 WO2022074153A1 (fr) 2020-10-07 2021-10-07 Plaque en alliage d'aluminium laminé et procédé de fabrication de ladite plaque
JP2023519155A JP2023544696A (ja) 2020-10-07 2021-10-07 圧延アルミニウム合金製板材およびこの板材の製造方法

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP20200645.8A EP3981893A1 (fr) 2020-10-07 2020-10-07 Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque

Publications (1)

Publication Number Publication Date
EP3981893A1 true EP3981893A1 (fr) 2022-04-13

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EP20200645.8A Withdrawn EP3981893A1 (fr) 2020-10-07 2020-10-07 Plaque d'un alliage d'aluminium laminé et fabrication d'une telle plaque
EP21798573.8A Pending EP4225959A1 (fr) 2020-10-07 2021-10-07 Plaque en alliage d'aluminium laminé et procédé de fabrication de ladite plaque

Family Applications After (1)

Application Number Title Priority Date Filing Date
EP21798573.8A Pending EP4225959A1 (fr) 2020-10-07 2021-10-07 Plaque en alliage d'aluminium laminé et procédé de fabrication de ladite plaque

Country Status (5)

Country Link
US (1) US20230372986A1 (fr)
EP (2) EP3981893A1 (fr)
JP (1) JP2023544696A (fr)
CN (1) CN116324005A (fr)
WO (1) WO2022074153A1 (fr)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3642542A (en) * 1970-02-25 1972-02-15 Olin Corp A process for preparing aluminum base alloys
EP1614760A1 (fr) 2003-04-15 2006-01-11 Nippon Light Metal Company Ltd. Plaque d'alliage d'aluminium presentant une excellente formabilite de pressage et une excellente soudabilite par points presentant une resistance continue, ainsi que methode pour sa production
CN104711499A (zh) * 2013-12-16 2015-06-17 北京有色金属研究总院 一种适用于含Zn的6XXX系铝合金的多级均匀化热处理方法
EP3018226A1 (fr) * 2014-11-05 2016-05-11 Constellium Valais SA (AG, Ltd) Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion
US20170073802A1 (en) * 2014-03-27 2017-03-16 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Forged aluminum alloy material and method for producing same
CN110629075A (zh) * 2018-06-25 2019-12-31 宝山钢铁股份有限公司 一种高强度高延伸率铝合金板材及其制造方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3642542A (en) * 1970-02-25 1972-02-15 Olin Corp A process for preparing aluminum base alloys
EP1614760A1 (fr) 2003-04-15 2006-01-11 Nippon Light Metal Company Ltd. Plaque d'alliage d'aluminium presentant une excellente formabilite de pressage et une excellente soudabilite par points presentant une resistance continue, ainsi que methode pour sa production
CN104711499A (zh) * 2013-12-16 2015-06-17 北京有色金属研究总院 一种适用于含Zn的6XXX系铝合金的多级均匀化热处理方法
US20170073802A1 (en) * 2014-03-27 2017-03-16 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Forged aluminum alloy material and method for producing same
EP3018226A1 (fr) * 2014-11-05 2016-05-11 Constellium Valais SA (AG, Ltd) Produits à très haute résistance forgés à partir d'alliages d'aluminium 6xxx ayant une excellente résistance à la corrosion
CN110629075A (zh) * 2018-06-25 2019-12-31 宝山钢铁股份有限公司 一种高强度高延伸率铝合金板材及其制造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
FRIEDRICH OSTERMANN: "Anwendungstechnologie Aluminium", 2014, pages: 175

Also Published As

Publication number Publication date
EP4225959A1 (fr) 2023-08-16
US20230372986A1 (en) 2023-11-23
CN116324005A (zh) 2023-06-23
JP2023544696A (ja) 2023-10-25
WO2022074153A1 (fr) 2022-04-14

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