EP3848476A1 - Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip - Google Patents
Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip Download PDFInfo
- Publication number
- EP3848476A1 EP3848476A1 EP20190782.1A EP20190782A EP3848476A1 EP 3848476 A1 EP3848476 A1 EP 3848476A1 EP 20190782 A EP20190782 A EP 20190782A EP 3848476 A1 EP3848476 A1 EP 3848476A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- strip
- sheet
- weight
- aluminum alloy
- gpi
- 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.)
- Pending
Links
Images
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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold 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
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet 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
- C22C21/06—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
- C22F1/047—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 a sheet metal or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, its use and a method for producing the sheet metal or strip.
- the invention has therefore set itself the task of making available an Al-Mg-aluminum alloy which has a high temperature-hardening reaction, in particular a lacquer stoving reaction (PBR).
- PBR lacquer stoving reaction
- this Al-Mg-aluminum alloy should be able to achieve comparatively high strengths.
- the invention solves the problem set according to the features of claim 1.
- Mg magnesium
- Zn zinc
- a degree of sheet metal deformation of 2% with a paint baking reaction at 185 ° C for 20 minutes an R p0.2 gain in strength of well over 150 MPa could be achieved - which is unknown even from PBR-optimized 6xxx alloys.
- this Al-Mg-Zn alloy reacts in the T4-FH condition, namely the solution-annealed, accelerated cooled (preferably quenched), stabilization annealed and cold-age-aged Al-Mg-Zn alloy, particularly rapidly hardening to a paint baking process - for example through a preferred formation of stable precursors of the T phase (Mg 32 (Al, Zn) 49 or Mg 3 Zn 3 Al 2 ) during the stabilization annealing treatment, which develop in the course of the paint-bake cycle into precipitations with a strong hardening effect and thus cause a particularly strong paint bake response (PBR).
- T phase Mg 32 (Al, Zn) 49 or Mg 3 Zn 3 Al 2
- the formation of the same phases or clusters in the size range from 1 to 10 nm suppresses the precipitation of S-phase and ⁇ -phase due to the comparatively high Zn content.
- these phases or clusters produced enable a significant increase in strength in the course of a post-curing reaction, for example a paint baking reaction at 185 ° C. for 20 minutes.
- this aluminum alloy according to the invention in the T4-FH state is energy-efficient in utilizing the available thermal energies in subsequent production steps due to the comparatively high artificial hardening reaction.
- the sheet or strip can have one or more elements: from 0 to 0.8% by weight of copper (Cu) and / or from 0 to 0.2% by weight of silver (Ag) and / or from 0 to 1 , 0 wt .-% manganese (Mn) and / or from 0 to 0.45 wt .-% silicon (Si) and / or from 0 to 0.55 wt .-% iron (Fe) and / or from 0 to 0.35% by weight chromium (Cr) and / or from 0 to 0.2% by weight titanium (Ti) and / or from 0 to 0.8% by weight zirconium (Zr) and / or from 0 to 1.0% by weight of hafnium (Hf) and / or from 0 to 0.3% by weight of niobium (Cu) and / or from 0 to 0.2% by weight of silver (Ag) and / or from 0 to 1 , 0 wt .-% manganese
- a vehicle is to be understood as meaning a land, water and / or air vehicle, for example.
- a heat treatment for example a thermal shock
- T4 treatment solution annealed with cold aging or cold aging
- a high PBR can be made possible if the aluminum alloy contains from 3.0 to 4.0% by weight of Zn, in particular from 3.3 to 3.7% by weight of Zn - in particular because, in combination with magnesium, a comparatively very favorable curing potential can be set.
- the alloy in the T4-FH condition has a comparatively high yield strength compared to a Zn-free alloy, which is significantly increased after subsequent reshaping and enamel baking.
- the above can be further improved when the aluminum alloy contains from 4.5 to 5.0% by weight of Mg.
- Mg contains from 4.5 to 5.0% by weight of Mg.
- PBR hardening potential
- the aluminum alloy has 0.3 to 0.6% by weight, in particular 0.4 to 0.6% by weight, for example 0.5 to 0.6% by weight, Cu.
- the aluminum alloy can preferably contain from 0.1 to 0.3% by weight of silver (Ag).
- Ag silver
- This proposed Ag content leads - similar to Cu - to an additional higher precipitation density in the course of the stabilization annealing treatment - and enables a further increase in the PBR.
- the aluminum alloy can preferably contain from 0.05 to 0.25% by weight of iron (Fe) in order to permit an increased proportion of secondary aluminum in the alloy.
- the aluminum alloy can preferably contain from 0.3 to 1.0% by weight of manganese (Mn).
- the aluminum alloy preferably has from 0.3 to 0.5% by weight of manganese (Mn).
- Mn manganese
- the aluminum alloy can preferably contain from 0.05 to 0.15% by weight of titanium (Ti) in order, for example, to adjust the grain size in a controlled manner.
- a sheet metal or strip according to the invention with a thickness of 0.5 to 4 mm, in particular 0.8 to 2.5 mm, can also be especially suitable for the production of molded parts of a vehicle, for example a motor vehicle.
- the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at least 0.25 ⁇ 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone, measured using Felfer's evaluation method (cf. P.
- the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at most 5.0 ⁇ 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone .
- the sheet metal or strip according to the invention can be suitable for a vehicle part, preferably a body part.
- the stabilization annealing treatment is preferably carried out at 95 ° C. (degrees Celsius) to 125 ° C. for at least 20 minutes (minutes) and a maximum of 10 hours (hours) in order to get through this Temperature control to prepare the sheet or strip reproducibly for a comparatively high artificial curing reaction, in particular paint bake response (PBR).
- This artificial hardening reaction for example PBR, can be increased further if the stabilization annealing treatment is carried out at 100 ° C. to 120 ° C. and / or for at least 2 h and a maximum of 4 h.
- the solution heat treatment is carried out at 450 ° C. to 500 ° C., in particular at 460 ° C. to 490 ° C. Recrystallization can also occur in the course of the solution treatment.
- the accelerated cooling takes place with a cooling rate of the sheet or strip of at least 10 ° C / s.
- the accelerated cooling is preferably carried out at a cooling rate of at least 20 ° C./s.
- under certified cooling is a faster cooling than cooling at room temperature and still air (cf. Friedrich Ostermann, Application Technology Aluminum, 3rd edition, published in 2014: Cooling after solution annealing en).
- the hot rolling is preferably carried out at a temperature of the sheet or strip of 310 ° C. to a maximum of 440 ° C. in order, for example, to reliably avoid edge cracks and crocodiling during hot rolling.
- the method according to the invention can therefore be particularly process-reliable.
- the advantages according to the invention with regard to high deformability for complex geometry and high yield point R p0.2 can turn out to be particularly advantageous if the aluminum sheet or strip in question is used for, in particular cold forming, in particular sheet metal forming, and subsequent hot curing, in particular stoving, preferably lacquer stoving, to form a molded part, in particular a vehicle part, preferably a body part, for example the outer skin, in a vehicle.
- Advantageous process conditions can result if the varnish is baked at 150 ° C. to 200 ° C. for at least 10 and a maximum of 30 minutes, in particular at 170 ° C. to 190 ° C. for at least 15 and a maximum of 25 minutes.
- Alloy 1 is a known AA5182 alloy as a reference alloy.
- Alloys 2 to 4 represent alloys according to the invention and contain balanced contents of Zn, Zn + Cu or Zn + Cu + Ag. The remainder of all alloys is aluminum and impurities that are unavoidable due to the manufacturing process, each with a maximum of 0.05% by weight and a total of 0.15% by weight. If necessary, alloys 1 to 4 can also contain 0.1% by weight of chromium (Cr).
- the alloys listed in Table 1 were examined with regard to their mechanical properties R p0.2 and elongation at break A by means of a tensile test. The tests were carried out in the T4-FH condition as well as after the paint baking cycle (PB) with a previous 2% reshaping. In addition, the density of Guinier Preston I zones (GPI zones) with at least 700 atoms per GPI zone was measured using the Felfer evaluation method using atomic probe tomography (atomic probe of the LEAP 3000HR type) as already described above . Table 2: Characteristic values of the alloys examined.
- the aluminum alloys 2 to 4 according to the invention achieve an unexpectedly high paint bake response (PBR) of up to 195 MPa compared to alloy 1 without the formability (or elongation) in the T4-FH state to deteriorate significantly.
- PBR paint bake response
- the alloys according to the invention, in combination with the production method according to the invention are particularly suitable for molded parts of a body.
- alloys according to the invention show a delayed onset of the PLC effect and thus a reduction in flow figures of type B.
- alloys 2 to 4 in the T4-FH state have an increasing density of Guinier-Preston I zones (GPI zones) with at least 700 atoms per GPI zone
- this density increasing Guinier-Preston I zones (GPI zones) with at least 700 atoms per GPI zone is designated in Table 2 as GPI zone density *.
- GPI zone density * of 1.6 ⁇ 10 23 GPI zones / m 3 already showed a surprisingly high R p0.2 gain in strength after the PB of over 400 MPa, as can be seen in alloy 3, which in Alloy 4 turns out to be even higher.
- a maximum density of Guinier-Preston I zones of 5 ⁇ 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone can be sufficient.
Landscapes
- 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)
- Laminated Bodies (AREA)
- Body Structure For Vehicles (AREA)
- Coating With Molten Metal (AREA)
- Metal Rolling (AREA)
- Paints Or Removers (AREA)
- Electroplating Methods And Accessories (AREA)
- Preventing Corrosion Or Incrustation Of Metals (AREA)
- Bending Of Plates, Rods, And Pipes (AREA)
- Application Of Or Painting With Fluid Materials (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Gasket Seals (AREA)
Abstract
Es werden betrifft ein Blech oder Band aus einer aushärtbaren Aluminiumlegierung, ein daraus gefertigtes Fahrzeugteil, eine Verwendung und ein Verfahren zur Herstellung des Blechs oder Bands. Um eine hohe Lackeinbrennreaktion (PBR) sicherzustellen wird vorgeschlagen, dass die Aluminiumlegierung von 4,0 bis 5,5 Gew.-% Magnesium (Mg) und von 2,5 bis 5,5 Gew.-% Zink (Zn) aufweist und sich im Zustand T4-FH befindet, wobei Gew.-% Magnesium (Mg) > Gew.-% Zink (Zn) ist. It relates to a sheet metal or strip made of a hardenable aluminum alloy, a vehicle part manufactured therefrom, a use and a method for producing the sheet metal or strip. In order to ensure a high paint stoving reaction (PBR), it is proposed that the aluminum alloy contain from 4.0 to 5.5% by weight magnesium (Mg) and from 2.5 to 5.5% by weight zinc (Zn) is in the T4-FH state, where% by weight magnesium (Mg)>% by weight zinc (Zn).
Description
Die Erfindung betrifft ein Blech oder Band aus einer aushärtbaren Aluminiumlegierung, ein daraus gefertigtes Fahrzeugteil, dessen Verwendung und ein Verfahren zur Herstellung des Blechs oder Bands.The invention relates to a sheet metal or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, its use and a method for producing the sheet metal or strip.
Um bei einem Aluminiumblech sowohl eine hohe Verformbarkeit beim Umformen bzw. Blechumformen, als auch eine vergleichsweise hohe Festigkeit nach einem Einbrennzyklus (beispielsweise bei einem KTL-Verfahren) zu ermöglichen, schlägt die
Nachteilig zeigt sich bei der in der
A disadvantage is shown in the
Zudem ist aus der
Dieser Umstand schließt derzeit Al-Mg-Aluminiumlegierung für Bauteile, die eine hohe Festigkeit im Einsatzzustand benötigen aus - dies, obwohl Al-Mg-Aluminiumlegierungen im Vergleich mit 6xxx-Legierungen besser umformbar wären.This circumstance currently excludes Al-Mg-aluminum alloys for components that require high strength in the operational state - although Al-Mg-aluminum alloys are better formable compared to 6xxx alloys.
Die Erfindung hat sich daher die Aufgabe gestellt, eine Al-Mg-Aluminiumlegierung zur Verfügung zu stellen, die eine hohe Warmaushärtereaktion, insbesondere Lackeinbrennreaktion (PBR), aufweist. Zudem soll diese Al-Mg-Aluminiumlegierung vergleichsweise hohe Festigkeiten erreichen können.The invention has therefore set itself the task of making available an Al-Mg-aluminum alloy which has a high temperature-hardening reaction, in particular a lacquer stoving reaction (PBR). In addition, this Al-Mg-aluminum alloy should be able to achieve comparatively high strengths.
Die Erfindung löst die gestellte Aufgabe nach den Merkmalen des Anspruchs 1.The invention solves the problem set according to the features of claim 1.
Die in den Legierungselementen von 4,0 bis 5,5 Gew.-% Magnesium (Mg) und von 2,5 bis 5,5 Gew.-% Zink (Zn), ausgewogene Aluminiumlegierung im Zustand T4-FH, nämlich den Zustand T4 mit einer Stabilisierungsglühbehandlung, wobei Gew.-% Magnesium (Mg) > Gew.-% Zink (Zn) ist, zeigt überraschend eine besonders hohe Warmaushärtereaktion.
So konnte bei einem Blechumformgrad von 2 % mit einer Lackeinbrennreaktion bei 185 °C für 20 Minuten ein Rp0,2-Festigkeits-Zugewinn von weit über 150 MPa erreicht werden - was selbst von, auf PBR-optimierten 6xxx Legierungen unbekannt ist. Offensichtlich reagiert diese Al-Mg-Zn-Legierung im Zustand T4-FH, nämlich die lösungsgeglühte, beschleunigt abgekühlte (vorzugsweise abgeschreckte), stabilisierungsglühbehandelte und kaltausgelagerte Al-Mg-Zn-Legierung, besonders schnellaushärtend auf ein Lackeinbrennen - beispielsweise durch eine bevorzugte Bildung von stabilen Vorläufern der T-Phase (Mg32(Al,Zn)49 bzw. Mg3Zn3Al2) während der Stabilisierungsglühbehandlung, welche sich im Zuge des Lackeinbrennen ("paint-bake cycle") zu stark härtend wirkenden Ausscheidungen weiterentwickeln und damit eine besonders starke Lackeinbrennreaktion ("Paint Bake Response" bzw. PBR) hervorrufen. Gleichzeitig wird durch die Bildung ebenjener Phasen bzw. Clustern im Größenbereich von 1 bis 10 nm die Ausscheidung von S-Phase und β-Phase aufgrund des, vergleichsweise hohen Zn-Gehalts unterdrückt. Im Gegensatz zu einem nicht stabilisierungsglühbehandelten Blech oder Band ermöglichen diese erzeugten Phasen bzw. Cluster eine deutliche Festigkeitssteigerung im Zuge einer Warmaushärtereaktion, beispielsweise Lackeinbrennreaktion bei 185 °C für 20 Minuten. Außerdem ist diese erfindungsgemäße Aluminiumlegierung im Zustand T4-FH aufgrund der vergleichsweise hohen Warmaushärtereaktion energieeffizient in der Ausnützung der zur Verfügung stehenden Wärmeenergien in nachfolgenden Herstellungsschritten.
Die erfindungsgemäße Aluminiumlegierung kann somit eine besonders gute Eignung zur Herstellung eines Formteils eines Fahrzeugs, vorzugsweise Karosserieteils, beispielsweise der Außenhaut, aufweisen.
Optional kann das Blech oder Band ein oder mehrere Elemente aufweisen: von 0 bis 0,8 Gew.-% Kupfer (Cu) und/oder von 0 bis 0,2 Gew.-% Silber (Ag) und/oder von 0 bis 1,0 Gew.-% Mangan (Mn) und/oder von 0 bis 0,45 Gew.-% Silizium (Si) und/oder von 0 bis 0,55 Gew.-% Eisen (Fe) und/oder von 0 bis 0,35 Gew.-% Chrom (Cr) und/oder von 0 bis 0,2 Gew.-% Titan (Ti) und/oder von 0 bis 0,8 Gew.-% Zirkon (Zr) und/oder von 0 bis 1,0 Gew.-% Hafnium (Hf) und/oder von 0 bis 0,3 Gew.-% Niob (Nb) und/oder von 0 bis 0,25 Gew.-% Tantal (Ta) und/oder von 0 bis 0,2 Gew.-% Vanadium (V).
Als Rest weist die Aluminiumlegierung Aluminium sowie herstellungsbedingt unvermeidbare Verunreinigungen mit jeweils maximal 0,05 Gew.-% und gesamt höchstens 0,15 Gew.-% auf.The aluminum alloy balanced in the alloy elements from 4.0 to 5.5% by weight magnesium (Mg) and from 2.5 to 5.5% by weight zinc (Zn), in the state T4-FH, namely the state T4 with a stabilization annealing treatment, where% by weight magnesium (Mg)>% by weight zinc (Zn), surprisingly shows a particularly high artificial hardening reaction.
For example, with a degree of sheet metal deformation of 2% with a paint baking reaction at 185 ° C for 20 minutes, an R p0.2 gain in strength of well over 150 MPa could be achieved - which is unknown even from PBR-optimized 6xxx alloys. Obviously, this Al-Mg-Zn alloy reacts in the T4-FH condition, namely the solution-annealed, accelerated cooled (preferably quenched), stabilization annealed and cold-age-aged Al-Mg-Zn alloy, particularly rapidly hardening to a paint baking process - for example through a preferred formation of stable precursors of the T phase (Mg 32 (Al, Zn) 49 or Mg 3 Zn 3 Al 2 ) during the stabilization annealing treatment, which develop in the course of the paint-bake cycle into precipitations with a strong hardening effect and thus cause a particularly strong paint bake response (PBR). At the same time, the formation of the same phases or clusters in the size range from 1 to 10 nm suppresses the precipitation of S-phase and β-phase due to the comparatively high Zn content. Unlike one, not Stabilization annealed sheet or strip, these phases or clusters produced enable a significant increase in strength in the course of a post-curing reaction, for example a paint baking reaction at 185 ° C. for 20 minutes. In addition, this aluminum alloy according to the invention in the T4-FH state is energy-efficient in utilizing the available thermal energies in subsequent production steps due to the comparatively high artificial hardening reaction.
The aluminum alloy according to the invention can thus have a particularly good suitability for producing a molded part of a vehicle, preferably a body part, for example the outer skin.
Optionally, the sheet or strip can have one or more elements: from 0 to 0.8% by weight of copper (Cu) and / or from 0 to 0.2% by weight of silver (Ag) and / or from 0 to 1 , 0 wt .-% manganese (Mn) and / or from 0 to 0.45 wt .-% silicon (Si) and / or from 0 to 0.55 wt .-% iron (Fe) and / or from 0 to 0.35% by weight chromium (Cr) and / or from 0 to 0.2% by weight titanium (Ti) and / or from 0 to 0.8% by weight zirconium (Zr) and / or from 0 to 1.0% by weight of hafnium (Hf) and / or from 0 to 0.3% by weight of niobium (Nb) and / or from 0 to 0.25% by weight of tantalum (Ta) and / or of 0 to 0.2 wt% vanadium (V).
The remainder of the aluminum alloy has aluminum and impurities that are unavoidable due to the manufacturing process, each with a maximum of 0.05% by weight and a total of 0.15% by weight.
Im Allgemeinen wird erwähnt, dass unter Fahrzeug beispielsweise ein Land-, Wasser- und/oder Luftfahrzeug zu verstehen ist.
Bekanntermaßen wird zum Erreichen des Zustands T4-FH die Legierung zusätzlich zu einer T4 Behandlung (= lösungsgeglüht mit Kaltauslagerung bzw. Kaltaushärtung) einer Wärmebehandlung, beispielsweise einem Wärmestoß, nach dem Lösungsglühen und beschleunigten Abkühlen unterworfen und danach kaltausgelagert. Weitere Beispiele für solch eine Stabilisierungsglühbehandlung sind aus der Literatur (vgl.
Aus
As is known, to achieve the T4-FH condition, the alloy is subjected to a heat treatment, for example a thermal shock, after the solution heat treatment and accelerated cooling, in addition to a T4 treatment (= solution annealed with cold aging or cold aging) and then cold aged. Further examples of such a stabilization annealing treatment can be found in the literature (cf.
Out
Ein hoher PBR kann ermöglicht werden, wenn die Aluminiumlegierung von 3,0 bis 4,0 Gew.-% Zn, insbesondere von 3,3 bis 3,7 Gew.-% Zn, aufweist - insbesondere, weil in Kombination mit Magnesium ein vergleichsweise sehr günstiges Aushärtepotenzial eingestellt werden kann. Zudem weist die Legierung im Zustand T4-FH eine gegenüber einer Zn-freien Legierung eine vergleichsweise hohe Dehngrenze auf, welche nach darauffolgendem Umformen und Lackeinbrennen deutlich erhöht wird.A high PBR can be made possible if the aluminum alloy contains from 3.0 to 4.0% by weight of Zn, in particular from 3.3 to 3.7% by weight of Zn - in particular because, in combination with magnesium, a comparatively very favorable curing potential can be set. In addition, the alloy in the T4-FH condition has a comparatively high yield strength compared to a Zn-free alloy, which is significantly increased after subsequent reshaping and enamel baking.
Vorstehendes ist weiter verbesserbar, wenn die Aluminiumlegierung von 4,5 bis 5,0 Gew.-% Mg aufweist. Dies kann einerseits in Kombination mit Zn zu einem günstigen Aushärtepotenzial, nämlich PBR, und andererseits zu einer sehr guten Umformbarkeit durch das im Al-Mischkristall zwangsgelöste Mg führen.The above can be further improved when the aluminum alloy contains from 4.5 to 5.0% by weight of Mg. On the one hand, in combination with Zn, this can lead to a favorable hardening potential, namely PBR, and, on the other hand, to very good formability due to the Mg forcibly dissolved in the Al mixed crystal.
Dies insbesondere, wenn die Aluminiumlegierung von 0,3 bis 0,6 Gew.-%, insbesondere 0,4 bis 0,6 Gew.-%, beispielsweise 0,5 bis 0,6 Gew.-%, Cu aufweist.
Derart kann beispielsweise eine Erhöhung der Ausscheidungsdichte im Zuge der Stabilisierungsglühbehandlung erreicht und eine weitere Erhöhung des PBR ermöglicht werden.
Vorzugsweise gilt bei einem Cu-Gehalt von > 0,5 Gew.-%, dass der Gehalt an Zn die Bedingung erfüllt: Zn=7.2-3.4*Cu [Gew.-%].This is particularly the case when the aluminum alloy has 0.3 to 0.6% by weight, in particular 0.4 to 0.6% by weight, for example 0.5 to 0.6% by weight, Cu.
In this way, for example, an increase in the precipitation density can be achieved in the course of the stabilization annealing treatment and a further increase in the PBR can be made possible.
With a Cu content of> 0.5% by weight, it preferably applies that the Zn content fulfills the condition: Zn = 7.2-3.4 * Cu [% by weight].
Vorzugsweise kann die Aluminiumlegierung von 0,1 bis 0,3 Gew.-% Silber (Ag) aufweisen. Dieser vorgeschlagene Gehalt an Ag führt - ähnlich wie bei Cu - zu einer zusätzlich höheren Ausscheidungsdichte im Zuge der Stabilisierungsglühbehandlung - und ermöglicht eine weitere Erhöhung des PBR.The aluminum alloy can preferably contain from 0.1 to 0.3% by weight of silver (Ag). This proposed Ag content leads - similar to Cu - to an additional higher precipitation density in the course of the stabilization annealing treatment - and enables a further increase in the PBR.
Vorzugsweise kann die Aluminiumlegierung von 0,05 bis 0,25 Gew.-% Eisen (Fe) aufweisen, um einen erhöhten Anteil an Sekundäraluminium an der Legierung zuzulassen.
Vorzugsweise kann die Aluminiumlegierung von 0,3 bis 1,0 Gew.-% Mangan (Mn) aufweisen. Vorzugsweise weist die Aluminiumlegierung von 0,3 bis 0,5 Gew.-% Mangan (Mn) auf. Mit dem vorgeschlagenen Gehalt an Mn kann unter anderem die Morphologie eisenhaltiger Phasen verändert werden, wodurch diese weniger duktilitätsmindernd wirken. Daneben erlauben erhöhte Mn-Gehalte die Einstellung kleinere Korngrößen, was der Umformbarkeit förderlich sein kann. Zudem kann der Gehalt an Mn zur Einstellung von geeigneten Primärphasen beitragen, Lüderslinien zu unterdrücken.
Vorzugsweise kann die Aluminiumlegierung von 0,05 bis 0,15 Gew.-% Titan (Ti) aufweisen, um beispielsweise die Korngröße kontrolliert einzustellen.The aluminum alloy can preferably contain from 0.05 to 0.25% by weight of iron (Fe) in order to permit an increased proportion of secondary aluminum in the alloy.
The aluminum alloy can preferably contain from 0.3 to 1.0% by weight of manganese (Mn). The aluminum alloy preferably has from 0.3 to 0.5% by weight of manganese (Mn). With the proposed Mn content, among other things, the morphology of iron-containing phases can be changed, so that these have less of a ductility-reducing effect. In addition, increased Mn contents allow smaller grain sizes to be set, which can be beneficial for formability. In addition, the Mn content can help establish suitable primary phases and suppress Lüders' lines.
The aluminum alloy can preferably contain from 0.05 to 0.15% by weight of titanium (Ti) in order, for example, to adjust the grain size in a controlled manner.
Ein erfindungsgemäßes Blech oder Band mit einer Dicke von 0,5 bis 4 mm, insbesondere von 0,8 bis 2,5 mm, kann sich speziell auch zur Herstellung von Formteilen eines Fahrzeugs, beispielsweise Kraftfahrzeugs, eignen.A sheet metal or strip according to the invention with a thickness of 0.5 to 4 mm, in particular 0.8 to 2.5 mm, can also be especially suitable for the production of molded parts of a vehicle, for example a motor vehicle.
Vorzugsweise weist die Aluminiumlegierung des Blechs oder Bands eine Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) von mindestens 0,25 x 1023 GPI-Zonen/m3 mit mindestens 700 Atomen pro GPI-Zone auf, gemessen unter Anwendung der Auswertemethode von Felfer (vgl.
Damit kann sichergestellt werden, dass Wachstums- bzw. entwicklungsfähige Vorläufer der T-Phase (Mg32(Al,Zn)49 bzw. Mg3Zn3Al2) in ausreichender Dichte und Größe vorhanden sind, um den Rp0,2-Festigkeits-Zugewinn im Zuge des Einbrennzyklus ("paint-bake cycle) sicherzustellen bzw. zu verbessern. Dies ist insbesondere dann der Fall, wenn die Aluminiumlegierung des Blechs oder Bands eine Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) von mindestens 1,5 x 1023 GPI-Zonen/m3 mit mindestens 700 Atomen pro GPI-Zone aufweist.Preferably, the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at least 0.25 × 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone, measured using Felfer's evaluation method (cf.
This ensures that precursors of the T phase (Mg 32 (Al, Zn) 49 or Mg 3 Zn 3 Al 2 ) capable of growth or development are present in sufficient density and size to achieve the R p0.2 strength -Gain in the course of the burn-in cycle ("paint-bake cycle). This is particularly the case when the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at least 1.5 x 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone.
Ausreichend kann zudem sein, wenn die Aluminiumlegierung des Blechs oder Bands eine Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) von höchstens 5,0 x 1023 GPI-Zonen/m3 mit mindestens 700 Atomen pro GPI-Zone aufweist.It can also be sufficient if the aluminum alloy of the sheet or strip has a density of Guinier-Preston I zones (GPI zones) of at most 5.0 × 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone .
Insbesondere kann sich das erfindungsgemäße Blech oder Band für ein Fahrzeugteil, vorzugsweise Karosserieteil eignen.In particular, the sheet metal or strip according to the invention can be suitable for a vehicle part, preferably a body part.
Ein Blech oder Band, das Formteile mit komplexer Geometrie und hoher Streckgrenze Rp0,2 ermöglicht, kann hergestellt werden, indem folgende Verfahrensschritte durchgeführt werden:
- Warmwalzen eines Walzbarrens zu einem warmgewalzten Blech oder Band; Kaltwalzen des warmgewalzten Blechs oder Bands auf eine Enddicke, optional mit einem Zwischenglühen des Blechs oder Bands,
- Wärmebehandlung des auf die Enddicke kaltgewalzten Blechs oder Bands, wobei die Wärmebehandlung umfasst:
- Lösungsglühen mit nachfolgendem, beschleunigtem Abkühlen, Stabilisierungsglühbehandlung des beschleunigt abgekühlten Blechs oder Bands und
- Kaltauslagerung des stabilisierungsglühbehandelten Blechs oder Bands. Erfindungsgemäß kann durch die Stabilisierungsglühbehandlung der erfindungsgemäßen Legierung deren schnelle Aushärtekinetik, hervorgerufen durch die Bildung stabiler Keime, welche für die starke Warmaushärtereaktion, insbesondere Lackeinbrennreaktion, verantwortlich sind, sichergestellt werden.
- Hot rolling a billet into a hot rolled sheet or strip; Cold rolling of the hot-rolled sheet or strip to a final thickness, optionally with intermediate annealing of the sheet or strip,
- Heat treatment of the sheet or strip cold-rolled to the final thickness, the heat treatment comprising:
- Solution annealing with subsequent accelerated cooling, stabilization annealing treatment of the accelerated cooled sheet or strip and
- Cold aging of the stabilization annealed sheet or strip. According to the invention, the stabilization annealing treatment of the alloy according to the invention can ensure its rapid hardening kinetics, caused by the formation of stable nuclei, which are responsible for the strong artificial hardening reaction, in particular the lacquer stoving reaction.
Vorzugsweise erfolgt die Stabilisierungsglühbehandlung bei 95 °C (Grad Celsius) bis 125 °C für mindestens 20 min (Minuten) und maximal 10 h (Stunden), um durch diese Temperaturführung das Blech oder Band reproduzierbar auf eine vergleichsweise hohe Warmaushärtereaktion, insbesondere Lackeinbrennreaktion (Paint Bake Response bzw. PBR), vorzubereiten. Diese Warmaushärtereaktion, beispielsweise PBR, kann weiter erhöht werden, wenn die Stabilisierungsglühbehandlung bei 100 °C bis 120 °C und/oder für mindestens 2 h und maximal 4 h erfolgt.The stabilization annealing treatment is preferably carried out at 95 ° C. (degrees Celsius) to 125 ° C. for at least 20 minutes (minutes) and a maximum of 10 hours (hours) in order to get through this Temperature control to prepare the sheet or strip reproducibly for a comparatively high artificial curing reaction, in particular paint bake response (PBR). This artificial hardening reaction, for example PBR, can be increased further if the stabilization annealing treatment is carried out at 100 ° C. to 120 ° C. and / or for at least 2 h and a maximum of 4 h.
Als vorteilhafte Verfahrensbedingungen können sich herausstellen, wenn das Lösungsglühen bei 450 °C bis 500 °C, insbesondere bei 460 °C bis 490 °C, erfolgt. Im Zuge des Lösungsglühens kann auch ein Rekristallisieren eintreten.It can turn out to be advantageous process conditions if the solution heat treatment is carried out at 450 ° C. to 500 ° C., in particular at 460 ° C. to 490 ° C. Recrystallization can also occur in the course of the solution treatment.
Um ein vergleichsweise hohes Aushärtepotenzial sicherzustellen, erfolgt das beschleunigte Abkühlen mit einer Abkühlrate des Blechs oder Bands von mindestens 10 °C/s. Vorzugsweise erfolgt das beschleunigte Abkühlen mit einer Abkühlrate von mindestens 20 °C/s. Insbesondere ist vorteilhaft, wenn das beschleunigte Abkühlen des Blechs oder Bands mit einer Abkühlrate von mindestens 10 °C/s dann erfolgt, wenn das Blech oder Band eine Temperatur beim Abkühlen unterhalb von 300 °C aufweist.
Im Allgemeinen wird erwähnt, dass unter bescheinigtem Abkühlen eine schnellere Abkühlung als eine Abkühlung bei Raumtemperatur und ruhender Luft ist (vgl.
In general, it is mentioned that under certified cooling is a faster cooling than cooling at room temperature and still air (cf.
Vorzugsweise erfolgt das Warmwalzen bei einer Temperatur des Blechs oder Bands von 310 °C bis maximal 440 °C, um beispielsweise Kantenrissen und Crocodiling beim Warmwalzen sicher zu vermeiden. Das erfindungsgemäße Verfahren kann daher besonders prozesssicher sein.The hot rolling is preferably carried out at a temperature of the sheet or strip of 310 ° C. to a maximum of 440 ° C. in order, for example, to reliably avoid edge cracks and crocodiling during hot rolling. The method according to the invention can therefore be particularly process-reliable.
Die erfindungsgemäßen Vorteile hinsichtlich hoher Verformbarkeit für komplexe Geometrie und hoher Streckgrenze Rp0,2, können sich als besonders vorteilhaft herausstellen, wenn das gegenständliche Aluminiumblech oder -band zum, insbesondere kalten, Umformen, insbesondere Blechumformen, und nachfolgenden Warmaushärten, insbesondere Einbrennen, vorzugsweise Lackeinbrennen, zu einem Formteil, insbesondere Fahrzeugteil, vorzugsweise Karosserieteil, beispielsweise der Außenhaut, in einem Fahrzeug verwendet wird. The advantages according to the invention with regard to high deformability for complex geometry and high yield point R p0.2 can turn out to be particularly advantageous if the aluminum sheet or strip in question is used for, in particular cold forming, in particular sheet metal forming, and subsequent hot curing, in particular stoving, preferably lacquer stoving, to form a molded part, in particular a vehicle part, preferably a body part, for example the outer skin, in a vehicle.
Vorteilhafte Verfahrensverhältnisse können sich ergeben, wenn das Lackeinbrennen bei 150 °C bis 200 °C für mindestens 10 und maximal 30 Minuten, insbesondere bei 170 °C bis 190 °C für mindestens 15 und maximal 25 Minuten, erfolgt.Advantageous process conditions can result if the varnish is baked at 150 ° C. to 200 ° C. for at least 10 and a maximum of 30 minutes, in particular at 170 ° C. to 190 ° C. for at least 15 and a maximum of 25 minutes.
Zum Nachweis der erzielten Effekte wurden beispielsweise gewalzte Halbzeuge, nämlich Feinbleche (welche auch zu einem Coil aufgewickelt sein können), aus verschiedenen Aluminiumlegierungen hergestellt - und zwar durch folgendes Verfahren:
- a. Warmwalzen des Walzbarrens zu einem warmgewalzten Blech oder Band bei 370 °C bis 430 °C
- b. Kaltwalzen des warmgewalzten Blechs oder Bands auf eine Enddicke 1,2 Millimeter (mm) mit einem Zwischenglühen bei 370 °C für eine 1 h mit anschließender Abkühlung bei Raumtemperatur
- c. Wärmebehandlung des auf die Enddicke kaltgewalzten Blechs oder Bands, in genannter Reihenfolge umfassend:
- i. Lösungsglühen bei 465 °C
- ii. nachfolgendes beschleunigtes Abkühlen (nämlich wasserunterstütztes Abschrecken)
mit mindestens 15 °C/s - iii. Stabilisierungsglühbehandlung des beschleunigt abgekühlten Blechs oder Bands bei 100 °C für 3 h
- iv. Kaltauslagerung des stabilisierungsglühbehandelten Blechs oder Bands für 3 Wochen bei Raumtemperatur (20 °C)
- a. Hot rolling the billet into a hot rolled sheet or strip at 370 ° C to 430 ° C
- b. Cold rolling of the hot-rolled sheet or strip to a final thickness of 1.2 millimeters (mm) with an intermediate annealing at 370 ° C. for 1 hour with subsequent cooling at room temperature
- c. Heat treatment of the sheet or strip cold-rolled to the final thickness, comprising in the order mentioned:
- i. Solution heat treatment at 465 ° C
- ii. subsequent accelerated cooling (namely water-assisted quenching) with at least 15 ° C / s
- iii. Stabilization annealing treatment of the accelerated cooled sheet or strip at 100 ° C. for 3 h
- iv. Cold aging of the stabilization annealed sheet or strip for 3 weeks at room temperature (20 ° C)
Diese Bleche werden nach der Kaltauslagerung im Zustand T4-FH jeweils zu einem Formteil, nämlich Karosserieteil der Außenhaut, durch Kaltblechumformen mit einem Umformgrad von 2 % umgeformt. Nach dem Umformen wurden diese Formteile einer kathodischen Tauchlackierung (KTL) mit einem Einbrennzyklus mit einer Einbrenntemperatur von 185 °C für 20 Minuten (min) unterworfen.
Bei der Legierungen 1 handelt es sich um eine bekannte AA5182-Legierung als Referenzlegierung. Die Legierungen 2 bis 4 stellen erfindungsgemäße Legierungen dar und enthalten ausgewogene Gehalte an Zn, Zn+Cu bzw. Zn+Cu+Ag.
Alle Legierungen weisen als Rest Aluminium sowie herstellungsbedingt unvermeidbare Verunreinigungen mit jeweils maximal 0,05 Gew.-% und gesamt höchstens 0,15 Gew.-% auf. Gegenfalls können die Legierungen 1 bis 4 noch 0,1 Gew.-% Chrom (Cr) enthalten.Alloy 1 is a known AA5182 alloy as a reference alloy. Alloys 2 to 4 represent alloys according to the invention and contain balanced contents of Zn, Zn + Cu or Zn + Cu + Ag.
The remainder of all alloys is aluminum and impurities that are unavoidable due to the manufacturing process, each with a maximum of 0.05% by weight and a total of 0.15% by weight. If necessary, alloys 1 to 4 can also contain 0.1% by weight of chromium (Cr).
Die in Tabelle 1 angeführten Legierungen wurden mittels Zugversuch hinsichtlich ihrer mechanischen Kennwerte Rp0.2 und Bruchdehnung A untersucht. Die Versuche erfolgten im T4-FH-Zustand sowie nach dem Lackeinbrennzyklus (PB) mit vorausgegangener 2%iger Umformung. Zudem wurde die Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) mit mindestens 700 Atomen pro GPI-Zone gemessen, und zwar unter Anwendung der Auswertemethode von Felfer unter Verwendung der Atomsondentomographie (Atomsonde vom Typ LEAP 3000HR) wie vorstehend bereits beschrieben.
Wie der Tabelle 2 zu entnehmen, erzielen die erfindungsgemäßen Aluminiumlegierungen 2 bis 4 im Vergleich zur Legierung 1 eine unerwartet hohe Lackeinbrennreaktion (Paint Bake Response bzw. PBR) von bis zu 195 MPa ohne die Umformbarkeit (bzw. Dehnung) im T4-FH-Zustand wesentlich zu verschlechtern. Aus diesem Grund weisen die erfindungsgemäßen Legierungen in Kombination mit dem erfindungsgemäßen Herstellverfahren eine besonders gute Eignung für Formteile einer Karosserie auf.As can be seen in Table 2, the aluminum alloys 2 to 4 according to the invention achieve an unexpectedly high paint bake response (PBR) of up to 195 MPa compared to alloy 1 without the formability (or elongation) in the T4-FH state to deteriorate significantly. For this reason, the alloys according to the invention, in combination with the production method according to the invention, are particularly suitable for molded parts of a body.
In
Umso überraschender ist weiter, dass nach dem Lackeinbrennen die Legierung 4, dargestellt in
Diese zu Legierung 4 beschriebenen Eigenschaften gilt auch für die anderen erfindungsgemäßen Legierungen 2 und 3.In
It is all the more surprising that after the lacquer baking, alloy 4, shown in FIG
These properties described for alloy 4 also apply to the other alloys 2 and 3 according to the invention.
Daneben zeigen die erfindungsgemäßen Legierungen ein verspätetes Einsetzten des PLC-Effektes und damit eine Verringerung von Fließfiguren des Typs B.In addition, the alloys according to the invention show a delayed onset of the PLC effect and thus a reduction in flow figures of type B.
Außerdem ist in der Tabelle 2 zu erkennen, dass die Legierungen 2 bis 4 im Zustand T4-FH eine zunehmende Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) mit mindestens 700 Atomen pro GPI-Zone aufweisen, wobei diese Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) mit mindestens 700 Atomen pro GPI-Zone in Tabelle 2 als GPI-Zone-Dichte* bezeichnet ist.
Bereits eine GPI-Zonen-Dichte* von 1,6 x 1023 GPI-Zonen/m3 zeigte einen überraschend hohen Rp0,2-Festigkeits-Zugewinn nach dem PB auf über 400 MPa, wie bei Legierung 3 zu erkennen, was bei Legierung 4 noch höher ausfällt.It can also be seen in Table 2 that alloys 2 to 4 in the T4-FH state have an increasing density of Guinier-Preston I zones (GPI zones) with at least 700 atoms per GPI zone, this density increasing Guinier-Preston I zones (GPI zones) with at least 700 atoms per GPI zone is designated in Table 2 as GPI zone density *.
A GPI zone density * of 1.6 × 10 23 GPI zones / m 3 already showed a surprisingly high R p0.2 gain in strength after the PB of over 400 MPa, as can be seen in alloy 3, which in Alloy 4 turns out to be even higher.
Bei allen Legierungen 2 bis 4 kann eine maximale Dichte an Guinier-Preston-I-Zonen (GPI-Zonen) von 5 x 1023 GPI-Zonen/m3 mit mindestens 700 Atomen pro GPI-Zone ausreichend sein.For all alloys 2 to 4, a maximum density of Guinier-Preston I zones (GPI zones) of 5 × 10 23 GPI zones / m 3 with at least 700 atoms per GPI zone can be sufficient.
Claims (17)
optional
optional
Priority Applications (9)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
IL294402A IL294402A (en) | 2020-01-07 | 2021-01-07 | Sheet or strip made of a hardenable aluminum alloy, a vehicle part made there-from, a use, and a method for producing the sheet or strip |
AU2021206534A AU2021206534A1 (en) | 2020-01-07 | 2021-01-07 | Sheet or strip made of an aluminum alloy which can be hardened, a vehicle part made therefrom, a use, and a method for producing the sheet or strip |
BR112022013432A BR112022013432A2 (en) | 2020-01-07 | 2021-01-07 | SHEET OR STRIP FROM A HARDENABLE ALUMINUM ALLOY, A VEHICLE PART MANUFACTURED FROM IT, USE AND PROCESS FOR PRODUCTION OF SHEET OR STRIP |
MX2022008360A MX2022008360A (en) | 2020-01-07 | 2021-01-07 | Sheet or strip made of an aluminum alloy which can be hardened, a vehicle part made therefrom, a use, and a method for producing the sheet or strip. |
PCT/EP2021/050203 WO2021140163A1 (en) | 2020-01-07 | 2021-01-07 | Sheet or strip made of an aluminum alloy which can be hardened, a vehicle part made therefrom, a use, and a method for producing the sheet or strip |
CN202180008190.XA CN115151667A (en) | 2020-01-07 | 2021-01-07 | Plate or strip made of a hardenable aluminum alloy, vehicle part produced therefrom, use and method for producing a plate or strip |
US17/791,147 US20230042050A1 (en) | 2020-01-07 | 2021-01-07 | Sheet or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, a use, and a method for producing the sheet or strip |
CA3166639A CA3166639A1 (en) | 2020-01-07 | 2021-01-07 | Sheet or strip made of a hardenable aluminum alloy, a vehicle part made therefrom, a use, and a method for producing the sheet or strip |
JP2022537081A JP2023509367A (en) | 2020-01-07 | 2021-01-07 | Plates or strips made of precipitation hardenable aluminum alloys, vehicle parts made from said plates or strips, uses of said plates or strips and methods for producing them |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP20150632 | 2020-01-07 |
Publications (1)
Publication Number | Publication Date |
---|---|
EP3848476A1 true EP3848476A1 (en) | 2021-07-14 |
Family
ID=69147498
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP20190782.1A Pending EP3848476A1 (en) | 2020-01-07 | 2020-08-12 | Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip |
Country Status (10)
Country | Link |
---|---|
US (1) | US20230042050A1 (en) |
EP (1) | EP3848476A1 (en) |
JP (1) | JP2023509367A (en) |
CN (1) | CN115151667A (en) |
AU (1) | AU2021206534A1 (en) |
BR (1) | BR112022013432A2 (en) |
CA (1) | CA3166639A1 (en) |
IL (1) | IL294402A (en) |
MX (1) | MX2022008360A (en) |
WO (1) | WO2021140163A1 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP4332260A1 (en) | 2022-09-05 | 2024-03-06 | AMAG rolling GmbH | Age-hardenable aluminium alloy, aluminium alloy metal strip or sheet, method for manufacturing this metal strip or sheet and its use in superplastic forming |
Citations (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4140556A (en) | 1976-04-16 | 1979-02-20 | Sumitomo Light Metal Industries, Ltd. | Aluminum alloy sheet |
JPS616244A (en) * | 1984-06-21 | 1986-01-11 | Sumitomo Light Metal Ind Ltd | High strength alloy for forming having fine grain and its manufacture |
JPS61179843A (en) * | 1985-02-04 | 1986-08-12 | Sumitomo Light Metal Ind Ltd | Aluminum alloy for magnetic disc superior in plating property |
JP2011184795A (en) * | 2010-02-12 | 2011-09-22 | Kobe Steel Ltd | Aluminum alloy sheet having excellent formability |
DE112011103667T5 (en) | 2010-11-05 | 2013-08-01 | Aleris Aluminum Duffel Bvba | Automobile molding of aluminum alloy product and process for its production |
JP5342201B2 (en) * | 2008-09-26 | 2013-11-13 | 株式会社神戸製鋼所 | Aluminum alloy plate with excellent formability |
US20170081749A1 (en) * | 2014-03-17 | 2017-03-23 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy sheet for structural components |
CN107022725A (en) * | 2017-04-20 | 2017-08-08 | 北京科技大学 | A kind of Technology for Heating Processing for improving ageing strengthening type Al Mg Zn alloy corrosion among crystalline grains |
US20170349989A1 (en) | 2014-11-11 | 2017-12-07 | Novelis Inc. | Multipurpose heat treatable aluminum alloys and related processes and uses |
US20180023174A1 (en) * | 2015-03-04 | 2018-01-25 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy sheet |
EP3521466A1 (en) * | 2015-10-30 | 2019-08-07 | Novelis Inc. | High strength 7xxx aluminum alloys and methods of making the same |
CN110541096A (en) * | 2019-09-11 | 2019-12-06 | 北京科技大学 | High-strength easy-to-weld Al-Mg-Zn-Cu alloy and preparation method thereof |
EP3690076A1 (en) * | 2019-01-30 | 2020-08-05 | Amag Rolling GmbH | Method for producing a metal sheet or strip made from aluminum alloy and a metal sheet, strip or moulded part produced thereby |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN104625571A (en) * | 2015-01-06 | 2015-05-20 | 湖南科技大学 | Age-hardening aluminum alloy cutting method |
CN104862551B (en) * | 2015-05-21 | 2017-09-29 | 北京科技大学 | Al Mg Cu Zn line aluminium alloys and aluminum alloy plate materials preparation method |
-
2020
- 2020-08-12 EP EP20190782.1A patent/EP3848476A1/en active Pending
-
2021
- 2021-01-07 BR BR112022013432A patent/BR112022013432A2/en unknown
- 2021-01-07 WO PCT/EP2021/050203 patent/WO2021140163A1/en active Application Filing
- 2021-01-07 CA CA3166639A patent/CA3166639A1/en active Pending
- 2021-01-07 MX MX2022008360A patent/MX2022008360A/en unknown
- 2021-01-07 CN CN202180008190.XA patent/CN115151667A/en active Pending
- 2021-01-07 US US17/791,147 patent/US20230042050A1/en active Pending
- 2021-01-07 IL IL294402A patent/IL294402A/en unknown
- 2021-01-07 AU AU2021206534A patent/AU2021206534A1/en active Pending
- 2021-01-07 JP JP2022537081A patent/JP2023509367A/en active Pending
Patent Citations (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4140556A (en) | 1976-04-16 | 1979-02-20 | Sumitomo Light Metal Industries, Ltd. | Aluminum alloy sheet |
JPS616244A (en) * | 1984-06-21 | 1986-01-11 | Sumitomo Light Metal Ind Ltd | High strength alloy for forming having fine grain and its manufacture |
JPS61179843A (en) * | 1985-02-04 | 1986-08-12 | Sumitomo Light Metal Ind Ltd | Aluminum alloy for magnetic disc superior in plating property |
JP5342201B2 (en) * | 2008-09-26 | 2013-11-13 | 株式会社神戸製鋼所 | Aluminum alloy plate with excellent formability |
JP2011184795A (en) * | 2010-02-12 | 2011-09-22 | Kobe Steel Ltd | Aluminum alloy sheet having excellent formability |
DE112011103667T5 (en) | 2010-11-05 | 2013-08-01 | Aleris Aluminum Duffel Bvba | Automobile molding of aluminum alloy product and process for its production |
US20170081749A1 (en) * | 2014-03-17 | 2017-03-23 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy sheet for structural components |
US20170349989A1 (en) | 2014-11-11 | 2017-12-07 | Novelis Inc. | Multipurpose heat treatable aluminum alloys and related processes and uses |
US20180023174A1 (en) * | 2015-03-04 | 2018-01-25 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy sheet |
EP3521466A1 (en) * | 2015-10-30 | 2019-08-07 | Novelis Inc. | High strength 7xxx aluminum alloys and methods of making the same |
CN107022725A (en) * | 2017-04-20 | 2017-08-08 | 北京科技大学 | A kind of Technology for Heating Processing for improving ageing strengthening type Al Mg Zn alloy corrosion among crystalline grains |
EP3690076A1 (en) * | 2019-01-30 | 2020-08-05 | Amag Rolling GmbH | Method for producing a metal sheet or strip made from aluminum alloy and a metal sheet, strip or moulded part produced thereby |
CN110541096A (en) * | 2019-09-11 | 2019-12-06 | 北京科技大学 | High-strength easy-to-weld Al-Mg-Zn-Cu alloy and preparation method thereof |
Non-Patent Citations (2)
Title |
---|
FRIEDRICH OSTERMANN: "Anwendungstechnologie Aluminium", 2014, pages: 175 |
P. FELFER ET AL.: "Detecting and extracting clusters in atom probe data: a simple, automated method using Voronoi cells", ULTRAMICROSCOPY, vol. 150, 2015, pages 30 - 36 |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP4332260A1 (en) | 2022-09-05 | 2024-03-06 | AMAG rolling GmbH | Age-hardenable aluminium alloy, aluminium alloy metal strip or sheet, method for manufacturing this metal strip or sheet and its use in superplastic forming |
Also Published As
Publication number | Publication date |
---|---|
JP2023509367A (en) | 2023-03-08 |
BR112022013432A2 (en) | 2022-09-13 |
MX2022008360A (en) | 2022-12-15 |
CN115151667A (en) | 2022-10-04 |
WO2021140163A1 (en) | 2021-07-15 |
AU2021206534A1 (en) | 2022-06-30 |
US20230042050A1 (en) | 2023-02-09 |
IL294402A (en) | 2022-08-01 |
CA3166639A1 (en) | 2021-07-15 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP3314031B1 (en) | High strength and easily reformable almg tape and method for producing the same | |
EP2770071B9 (en) | Aluminium alloy for the production of semi-finished products or components for motor vehicles, method for producing an aluminium alloy strip from this aluminium alloy and aluminium alloy strip and uses thereof | |
DE112004000596B4 (en) | High strength Al-Zn alloy and method of making such alloy product | |
DE1558521C3 (en) | Use of a nickel-chromium wrought alloy as a superplastic material | |
EP2449145B1 (en) | AlMgSi-sheet for applications with high shaping requirements | |
DE102005045341A1 (en) | High strength, high strength Al-Zn alloy product and method of making such a product | |
EP3176275B2 (en) | Aluminium-silicon die casting alloy method for producing a die casting component made of the alloy, and a body component with a die casting component | |
EP2570509B1 (en) | Production method for AlMgSi-aluminium strip | |
EP3825428B1 (en) | Die cast component and method for producing a die cast component | |
DE2714395A1 (en) | PROCESS FOR MANUFACTURING GOOD FORMABLE ZIPFEL ARMS ALUMINUM SHEETS WITH HIGH MECHANICAL STRENGTH | |
DE60300004T3 (en) | Kneaded product of Al-Cu-Mg alloy for the structural component of an aircraft | |
WO2002083967A1 (en) | Method for producing almn strips or sheets | |
DE2362658A1 (en) | STEEL SHEET WITH EXCELLENT PRESS FORMABILITY AND METHOD FOR MANUFACTURING IT | |
EP2888383B1 (en) | Aluminium alloy strip which is resistant to intercrystalline corrosion and method for producing same | |
DE2348249C2 (en) | Method of manufacturing silicon steel sheet with Goss texture | |
EP3848476A1 (en) | Sheet or strip made of a curable aluminium alloy, vehicle part manufactured from same, its use and a method for producing the sheet or strip | |
DE1284095B (en) | Process for producing aluminum alloy sheets with high creep rupture strength | |
EP1748088B1 (en) | Process for producing a semi-finished product or component for chassis or structural automotive applications | |
DE102019202676B4 (en) | Cast components with high strength and ductility and low tendency to hot crack | |
DE69702133T3 (en) | USE OF AN ALUMINUM SILICON MAGNESIUM ALLOY FOR THE MANUFACTURE OF VEHICLE CHASSIS PARTS AND METHOD OF THIS PREPARATION. | |
DE60310381T2 (en) | AL-MG ALLOY BRACKET OR TAPE FOR THE PRODUCTION OF CURVED PARTS WITH SMALL BENDING ADLER | |
EP3690076A1 (en) | Method for producing a metal sheet or strip made from aluminum alloy and a metal sheet, strip or moulded part produced thereby | |
DE10324453A1 (en) | Rolled heat-treatable Al-Mg-Si alloy product | |
EP3486343B1 (en) | Precipitation hardenable aluminium alloy | |
EP2426228B1 (en) | Magnesium sheet semi-finished products with improved cold reforming characteristics |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE APPLICATION HAS BEEN PUBLISHED |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20220114 |
|
RBV | Designated contracting states (corrected) |
Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
17Q | First examination report despatched |
Effective date: 20220912 |
|
P01 | Opt-out of the competence of the unified patent court (upc) registered |
Effective date: 20230514 |