EP1587965A1 - Aluminium alloy with increased resistance and low quench sensitivity - Google Patents
Aluminium alloy with increased resistance and low quench sensitivityInfo
- Publication number
- EP1587965A1 EP1587965A1 EP03789376A EP03789376A EP1587965A1 EP 1587965 A1 EP1587965 A1 EP 1587965A1 EP 03789376 A EP03789376 A EP 03789376A EP 03789376 A EP03789376 A EP 03789376A EP 1587965 A1 EP1587965 A1 EP 1587965A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- temperature
- max
- bars
- aluminum alloy
- cooling
- 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
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
- C22C21/10—Alloys based on aluminium with zinc 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
- C22F1/053—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 zinc 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
- C22F1/057—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 copper as the next major constituent
Definitions
- the invention relates to an aluminum alloy with high strength and low quench sensitivity.
- a method for producing thick plates from the aluminum alloy is also within the scope of the invention.
- hot-rolled and thermoset plates are usually used today. Larger molds with a thickness of more than 300 mm were either made from forged blocks or even directly from continuous cast ingots.
- a major disadvantage of the aluminum alloys used today for mold making is their high quenching sensitivity.
- the rate of cooling from the homogenization or solution annealing temperature must be increased with increasing plate thickness. Due to the high temperature gradients that occur between the surface and the core of the ingots or plates, the harmful internal stresses increase, so that for this reason alone there is a limit to a further increase in the cooling rate and thus to the strength level that can ultimately be achieved.
- the invention has for its object to provide a suitable for the production of thick plates with high strength level aluminum alloy with low To provide quench sensitivity.
- Another object of the invention is to provide a suitable method with which the aluminum alloy can be processed into thick plates with sufficiently high strength over the entire plate thickness.
- the composition of the alloy is selected such that it has a very low quenching sensitivity and nevertheless has an extraordinarily high level of strength. Thick cross sections can therefore be brought to a high level of strength with forced air cooling and precipitation hardening.
- an isotropic distribution of the residual stresses in the cross section of the plate is to be aimed for.
- the grain size and the shape of the grain in the plate are of importance for the reduction of the internal stresses. The finer and more uniform the crystals are, the better the internal stresses in the cross-section of the plate can balance.
- the grain boundaries act as sinks for dislocations when local stress peaks are reduced.
- the addition of zirconium can achieve a fine grain structure in the plate by selecting the rate at which the ingots heat up to the homogenization or solution annealing temperature in such a way that the most homogeneous distribution of submicron excretions of Al 3 Zr in the structure arises.
- the following two methods are particularly suitable for producing plates from the alloy according to the invention, which, depending on the desired thickness of the mold, lead to a hot-rolled and thermally hardened plate or to a thermally hardened continuous cast ingot used as a plate.
- the process for producing boards with a thickness of up to 300 mm is characterized by the following steps:
- a continuous cast ingot produced from the alloy according to the invention can be used directly as a plate.
- the procedure is characterized by the following steps:
- thermoset bars As plates.
- the ingot is preferably cooled from the homogenization temperature of 470 to 490 ° C. to the intermediate temperature of 400 to 410 ° C. in still air.
- the ingot should be cooled from the intermediate temperature of 400 to 410 ° C so quickly that the loss of strength is as low as possible.
- the cooling rate must not be too high, since otherwise the residual stresses will build up.
- the billets are cooled from the intermediate temperature of 400 to 410 ° C. to a temperature of less than 100 ° C. preferably using moving air (forced air cooling) or in a water / air spray.
- the bar thickness must also be taken into account. However, it is within the scope of professional action to determine the optimal cooling conditions for a given ingot format using simple tests.
- the low heating rate in the temperature range between 170 and 410 ° C. when the ingot is heated to the homogenization temperature is an essential feature of the process according to the invention.
- the AlZnMg equilibrium phase (T phase) is stable in the temperature range mentioned, which is also referred to as the heterogenization interval.
- the slow passage through the heterogenization interval leads to a finely dispersed separation of the T phase, the phase interfaces of the separated particles of the T phase forming preferred germ sites for the precipitation of Al 3 Zr particles starting at a temperature of about 350 ° C.
- the previously separated particles of the T phase dissolve and what remains is an even distribution of the fine, submicron A ⁇ Zr precipitates, which are preferably due to the original particle boundaries of the T phase and to subcom boundaries and so that there is a homogeneous distribution.
- These fine Al 3 Zr particles cause a strong growth inhibition in the recrystallization of the plates in solution annealing as well as in the homogenization annealing of cast ingots, and the desired isotropic grain structure in the ingot results.
- the grain-refining additional element Zr is thus optimally used.
- a further essential feature of the method according to the invention is the combined homogenization and solution annealing with subsequent two-stage cooling, whereas the usual methods according to the state of the art In order to achieve a strength that is still acceptable in the middle of the ingot, a separate solution annealing with subsequent quenching at a high cooling rate is required in the technology.
- cooling in moving air or “forced air cooling” is understood here to mean an air cooling which is usually supported by fans and which leads to a heat transfer coefficient on the bar surface of approximately 40 W / m 2 K. Cooling in a water / air spray leads to a somewhat higher heat transfer coefficient on the bar surface.
- the alloy according to the invention has a low quench sensitivity.
- the loss of strength in the plate core is smaller than in the prior art alloys, despite the relatively mild cooling conditions.
- this effect is much more pronounced for plates made directly from continuous cast ingots than for hot-rolled plates.
- the two-stage cooling from the homogenization temperature to room temperature has proven to be particularly advantageous for achieving a structure with low residual stresses.
- thermosetting room temperature storage
- a first heat treatment at a first temperature and a second heat treatment at a second temperature higher than the first temperature are preferably carried out in succession, e.g.
- Heat curing to the heat treatment state is particularly preferred
- the field of application of the alloy according to the invention and of the thick plates produced therefrom results from the range of properties described above.
- the plates are particularly suitable for mold making, ie for the production of plastic injection molds, but also generally for machine, tool and mold making.
- - Fig. 1 shows the distribution of Brinell hardness over part of the cross section of a continuous casting ingot with a cross section of 440 mm x 900 mm after fan cooling.
- the ingot was heated to a temperature of 480 ° C within 30 hours, taking care that the heating rate in the range between 170 and 410 ° C was less than 20 ° C / h.
- the ingot was homogenized to compensate for the solidification-induced crystal segregation by holding the ingot at 480 ° C. for 12 hours.
- the homogenized ingot was cooled in a first stage in still air from the homogenization temperature to an intermediate temperature of 400 ° C and then in a second stage with fans from 400 ° C to 100 ° C. The further cooling to room temperature was again carried out in resting air.
- the ingot was hot-cured at 95 ° C. for 8 hours and then at 155 ° C. for 18 hours to the over-hardened state T76.
- the Brinell hardness was determined over the cross-section of the bar on samples of the thermally hardened ingot sawed out perpendicular to the longitudinal direction of the ingot.
- the areas of the same hardness shown in FIG. 1 clearly show the slight loss of hardness or strength in the bar core compared to the bar surface.
- FIG. 2 shows the temperature-time curves for a fan cooling for the surface (O) and the core (K) of an ingot with a cross section of 440 ⁇ 900 mm
- FIG. 3 the gradients between the temperature T derived therefrom «In the bar core and the temperature To on the bar surface.
- FIGS. 4 and 5 show the corresponding curves for an ingot with a cross section of 1000 x 1200 mm. The results show that bars produced with the method according to the invention with a thickness of up to 1000 mm are still likely to meet the mechanical strength requirements placed on plates for the production of plastic injection molds.
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)
- Continuous Casting (AREA)
- Moulds For Moulding Plastics Or The Like (AREA)
- Metal Rolling (AREA)
- Investigating Or Analyzing Materials By The Use Of Fluid Adsorption Or Reactions (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Laminated Bodies (AREA)
- Conductive Materials (AREA)
- Contacts (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Safety Valves (AREA)
- Sampling And Sample Adjustment (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
Aluminiumlegierung mit hoher Festigkeit und geringer AbschreckempfindlichkeitAluminum alloy with high strength and low quench sensitivity
Die Erfindung betrifft eine Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit. Im Rahmen der Erfindung liegt auch ein Verfahren zur Herstellung dicker Platten aus der Aluminiumlegierung.The invention relates to an aluminum alloy with high strength and low quench sensitivity. A method for producing thick plates from the aluminum alloy is also within the scope of the invention.
Insbesondere in der Automobilindustrie besteht zunehmend ein Bedarf an grossen Kunststoffbauteilen, wie z.B. integrale Stossstangen. Zur Herstellung der entsprechend grossen Spritzgiessformen werden Platten benötigt, deren Dicke sehr oft 150 mm übersteigt und in gewissen Fällen sogar mehr als 500 mm beträgt.In the automotive industry in particular, there is an increasing need for large plastic components, such as integral bumpers. Plates are required to produce the correspondingly large injection molds, the thickness of which very often exceeds 150 mm and in some cases is even more than 500 mm.
Für den Bau von Spritzgiessformen mit einer Dicke von beispielsweise 50 bis 300 mm werden heute üblicherweise warmgewalzte und warmausgehärtete Platten eingesetzt. Grössere Formen mit einer Dicke von mehr als 300 mm wurden entweder aus geschmiedeten Blöcken oder auch schon direkt aus Stranggussbarren gefertigt.For the construction of injection molds with a thickness of, for example, 50 to 300 mm, hot-rolled and thermoset plates are usually used today. Larger molds with a thickness of more than 300 mm were either made from forged blocks or even directly from continuous cast ingots.
Ein wesentlicher Nachteil der heute für den Formenbau eingesetzten Aluminiumlegierungen ist deren hohe Abschreckempfindlichkeit. Damit die Barren oder Platten bei der Warmaushärtung das für Kunststoff-Spritzgiessformen geforderte Festigkeitsniveau erreichen, muss die Abkühlungsgeschwindigkeit von der Homogenisierungs- oder Lösungsglühtemperatur mit zunehmender Platten- dicke erhöht werden. Durch die hierbei auftretenden hohen Temperaturgradienten zwischen der Oberfläche und dem Kern der Barren oder Platten nehmen die schädlichen Eigenspannungen zu, so dass schon aus diesem Grund einer weiteren Erhöhung der Abkühlungsgeschwindigkeit und damit dem letztlich erreichbaren Festigkeitsniveau Grenzen gesetzt sind.A major disadvantage of the aluminum alloys used today for mold making is their high quenching sensitivity. In order for the ingots or plates to reach the strength level required for plastic injection molds during hot curing, the rate of cooling from the homogenization or solution annealing temperature must be increased with increasing plate thickness. Due to the high temperature gradients that occur between the surface and the core of the ingots or plates, the harmful internal stresses increase, so that for this reason alone there is a limit to a further increase in the cooling rate and thus to the strength level that can ultimately be achieved.
Der Erfindung liegt die Aufgabe zugrunde, eine zur Herstellung von dicken Platten mit hohem Festigkeitsniveau geeignete Aluminiumlegierung mit geringer Abschreckempfindlichkeit bereitzustellen.The invention has for its object to provide a suitable for the production of thick plates with high strength level aluminum alloy with low To provide quench sensitivity.
Ein weiteres Ziel der Erfindung liegt darin, ein geeignetes Verfahren anzugeben, mit dem die Aluminiumlegierung zu dicken Platten mit ausreichend hoher Festigkeit über die gesamte Plattendicke verarbeitet werden kann.Another object of the invention is to provide a suitable method with which the aluminum alloy can be processed into thick plates with sufficiently high strength over the entire plate thickness.
Zur erfindungsgemässen Lösung der Aufgabe führt eine Aluminiumlegierung mitAn aluminum alloy is used to achieve the object according to the invention
4,6 bis 5,2 Gew.-% Zn 2,6 bis 3,0 Gew.-% Mg4.6 to 5.2 wt% Zn 2.6 to 3.0 wt% Mg
0.1 bis 0,2 Gew.-% Cu 0,05 bis 0,2 Gew.-% Zr max. 0,05 Gew.-% Mn max. 0,05 Gew.-% Cr max. 0,15 Gew.-% Fe max. 0,15 Gew.-% Si max. 0,10 Gew.-% Ti0.1 to 0.2 wt% Cu 0.05 to 0.2 wt% Zr max. 0.05% by weight Mn max. 0.05% by weight Cr max. 0.15% by weight Fe max. 0.15% by weight Si max. 0.10 wt% Ti
und Aluminium als Rest mit herstellungsbedingten Verunreinigungen, einzeln max. 0,05 Gew.-%, insgesamt max. 0,15 Gew.-%.and aluminum as the rest with production-related impurities, individually max. 0.05% by weight, total max. 0.15% by weight.
Die Zusammensetzung der Legierung ist erfindungsgemäss so gewählt, dass sie eine sehr geringe Abschreckempfindlichkeit aufweist und trotzdem ein aus- serordentlich hohes Festigkeitsniveau besitzt. Dicke Querschnitte können daher mit forcierter Luftabkühlung und durch Ausscheidungshärtung auf ein hohes Festigkeitsniveau gebracht werden.According to the invention, the composition of the alloy is selected such that it has a very low quenching sensitivity and nevertheless has an extraordinarily high level of strength. Thick cross sections can therefore be brought to a high level of strength with forced air cooling and precipitation hardening.
Für die einzelnen Legierungselemente gelten die folgenden Vorzugsbereiche: 4,6 bis 4,8 Gew.-% Zn 2,6 bis 2,8 Gew.-% MgThe following preferred ranges apply to the individual alloy elements: 4.6 to 4.8% by weight of Zn 2.6 to 2.8% by weight of Mg
0,10 bis 0,15 Gew.-% Cu 0,08 bis 0,18 Gew.-% Zr max. 0,03 Gew.-% Mn max. 0,02 Gew.-% Cr max. 0,12 Gew.-% Fe max. 0,12 Gew.-% Si max. 0,05 Gew.-% Ti0.10 to 0.15 wt% Cu 0.08 to 0.18 wt% Zr Max. 0.03% by weight Mn max. 0.02% by weight Cr max. 0.12% by weight Fe max. 0.12% by weight Si max. 0.05% by weight of Ti
Für die Anwendung der erfindungsgemässen Legierung als Werkstoff für den Formenbau ist eine möglichst isotrope Verteilung der Eigenspannungen im Querschnitt der Platte anzustreben. Für den Abbau der Eigenspannungen ist u.a. die Korngrösse und die Kornform in der Platte von Bedeutung. Je feiner und gleichmässiger die Kristalle vorliegen, desto besser können sich die Eigenspannungen im Querschnitt der Platte ausgleichen. Die Korngrenzen wirken dabei als Senken für Versetzungen beim Abbau von lokalen Spannungsspitzen. Wie weiter unten erläutert, kann durch den Zusatz von Zirkonium ein feines Korngefüge in der Platte erreicht werden, indem man die Aufheizgeschwindigkeit der Barren auf die Homogenisierungs- bzw. Lösungsglühtemperatur so wählt, dass eine möglichst homogene Verteilung von submikronen Ausscheidungen von AI3Zr im Gefüge entsteht.For the use of the alloy according to the invention as a material for mold construction, an isotropic distribution of the residual stresses in the cross section of the plate is to be aimed for. The grain size and the shape of the grain in the plate are of importance for the reduction of the internal stresses. The finer and more uniform the crystals are, the better the internal stresses in the cross-section of the plate can balance. The grain boundaries act as sinks for dislocations when local stress peaks are reduced. As explained further below, the addition of zirconium can achieve a fine grain structure in the plate by selecting the rate at which the ingots heat up to the homogenization or solution annealing temperature in such a way that the most homogeneous distribution of submicron excretions of Al 3 Zr in the structure arises.
Zur Herstellung von Platten aus der erfindungsgemässen Legierung eignen sich insbesondere die folgenden zwei Verfahren, die je nach gewünschter Dicke der Form zu einer warmgewalzten und warmausgehärteten Platte oder zu einem als Platte verwendeten warmausgehärteten Stranggussbarren führen.The following two methods are particularly suitable for producing plates from the alloy according to the invention, which, depending on the desired thickness of the mold, lead to a hot-rolled and thermally hardened plate or to a thermally hardened continuous cast ingot used as a plate.
Zur Herstellung von Platten mit einer Dicke von bis zu 300 mm ist das Verfahren durch die folgenden Schritte gekennzeichnet:The process for producing boards with a thickness of up to 300 mm is characterized by the following steps:
A. Stranggiessen der Aluminiumlegierung zu Barren mit einer Dicke von mehr als 300 mm,A. Continuous casting of the aluminum alloy into bars with a thickness of more than 300 mm,
B. Aufheizen der Barren mit einer Aufheizgeschwindigkeit von max. 20°C/h zwischen 170 und 410°C auf eine Temperatur von 470 bis 490°C,B. heating the bars with a heating rate of max. 20 ° C / h between 170 and 410 ° C to a temperature of 470 to 490 ° C,
C. Homogenisieren der Barren während einer Zeitdauer von 10 bis 14 h bei einer Temperatur von 470 bis 490°C, D. Warmwalzen der homogenisierten Barren zu Platten,C. homogenizing the ingots over a period of 10 to 14 hours at a temperature of 470 to 490 ° C, D. hot rolling the homogenized ingots into sheets,
E. Abkühlen der Platten von einer Temperatur von 400 bis 410°C auf eine Temperatur von weniger als 100°C,E. cooling the plates from a temperature of 400 to 410 ° C to a temperature of less than 100 ° C,
F. Abkühlen der Platten auf Raumtemperatur, G. Warmaushärten der Platten.F. cooling the plates to room temperature, G. heat setting the plates.
Zur Herstellung von Platten mit einer Dicke von mehr als 300 mm und insbesondere von Platten mit einer Dicke von mehr als 500 mm kann ein aus der erfindungsgemässen Legierung hergestellter Stranggussbarren direkt als Platte verwendet werden. Das Verfahren ist in diesem Fall durch die folgenden Schritte gekennzeichnet:For the production of plates with a thickness of more than 300 mm and in particular of plates with a thickness of more than 500 mm, a continuous cast ingot produced from the alloy according to the invention can be used directly as a plate. In this case, the procedure is characterized by the following steps:
A. Stranggiessen der Legierung zu Barren mit einer Dicke von mehr als 300 mm,A. Continuous casting of the alloy into bars with a thickness of more than 300 mm,
B. Aufheizen der Barren mit einer Aufheizgeschwindigkeit von max. 20°C/h zwischen 170 und 410°C auf eine Temperatur von 470 bis 490°C,B. heating the bars with a heating rate of max. 20 ° C / h between 170 and 410 ° C to a temperature of 470 to 490 ° C,
C. Homogenisieren der Barren während einer Zeitdauer von 10 bis 14 h bei einer Temperatur von 470 bis 490°C,C. homogenizing the ingots over a period of 10 to 14 hours at a temperature of 470 to 490 ° C,
D. Abkühlen der Barren auf eine Zwischentemperatur von 400 bis 410 °C,D. cooling of the bars to an intermediate temperature of 400 to 410 ° C,
E. Abkühlen der Barren von der Zwischentemperatur von 400 bis 410°C auf eine Temperatur von weniger als 100°C,E. cooling of the bars from the intermediate temperature of 400 to 410 ° C to a temperature of less than 100 ° C,
F. Abkühlen der Barren auf Raumtemperatur,F. cooling the bars to room temperature,
G. Warmaushärten der Barren,G. hot hardening of the bars,
H. Verwenden der warmausgehärteten Barren als Platten.H. Use the thermoset bars as plates.
Bevorzugt erfolgt das Abkühlen der Barren von der Homogenisierungstemperatur von 470 bis 490°C auf die Zwischentemperatur von 400 bis 410 °C an ruhender Luft.The ingot is preferably cooled from the homogenization temperature of 470 to 490 ° C. to the intermediate temperature of 400 to 410 ° C. in still air.
Das Abkühlen der Barren von der Zwischentemperatur von 400 bis 410°C sollte einerseits so rasch erfolgen, dass der Festigkeitsverlust möglichst gering ist. Andererseits darf die Abkühlungsgeschwindigkeit auch nicht zu hoch sein, da sonst zu hohe Eigenspannungen aufgebaut werden. Das Abkühlen der Barren von der Zwischentemperatur von 400 bis 410°C auf eine Temperatur von weniger als 100°C erfolgt bevorzugt an bewegter Luft (forced air cooling) oder in einem Wasser/Luft-Sprühnebel.On the one hand, the ingot should be cooled from the intermediate temperature of 400 to 410 ° C so quickly that the loss of strength is as low as possible. On the other hand, the cooling rate must not be too high, since otherwise the residual stresses will build up. The billets are cooled from the intermediate temperature of 400 to 410 ° C. to a temperature of less than 100 ° C. preferably using moving air (forced air cooling) or in a water / air spray.
Bei der Wahl der Abkühlungsbedingungen muss auch die Barrendicke berücksichtigt werden. Es liegt jedoch im Rahmen des fachmännischen Handelns, für ein vorgegebenes Barrenformat die optimalen Abkühlungsbedingungen anhand einfacher Versuche zu ermitteln.When choosing the cooling conditions, the bar thickness must also be taken into account. However, it is within the scope of professional action to determine the optimal cooling conditions for a given ingot format using simple tests.
Die niedrige Aufheizgeschwindigkeit im Temperaturbereich zwischen 170 und 410°C beim Aufheizen der Barren auf die Homogenisierungstemperatur ist ein wesentliches Merkmal des erfindungsgemässen Verfahrens. Im erwähnten Temperaturbereich, der auch als Heterogenisierungsintervall bezeichnet wird, ist die AlZnMg-Gleichgewichtsphase (T-Phase) stabil. Das langsame Durch- laufen des Heterogenisierungsintervalls führt zu einem fein dispersen Ausscheiden der T-Phase, wobei die Phasengrenzflächen der ausgeschiedenen Teilchen der T-Phase bevorzugte Keimstellen für die bei einer Temperatur von etwa 350°C einsetzende Ausscheidung von AI3Zr-Teilchen bilden. Beim weiteren Aufheizen der Barren auf die Homogenisierungstemperatur lösen sich die zuvor ausgeschiedenen Teilchen der T-Phase auf und zurück bleibt eine gleichmässige Verteilung der feinen, submikronen A^Zr-Ausscheidungen, welche bevorzugt an den ursprünglichen Teilchengrenzen der T-Phase sowie an Subkomgrenzen liegen und damit eine homogene Verteilung ergeben. Diese feinen AI3Zr-Teilchen bewirken eine sowohl eine starke Wachstumshemmung bei der Rekristallisation der Platten bei der Lösungsglühung als auch bei der Homogenisierungsglühung von Gussbarren, und es resultiert das gewünschte isotrope Korngefüge im Barren. Das kornfeinende Zusatzelement Zr wird damit optimal genutzt.The low heating rate in the temperature range between 170 and 410 ° C. when the ingot is heated to the homogenization temperature is an essential feature of the process according to the invention. The AlZnMg equilibrium phase (T phase) is stable in the temperature range mentioned, which is also referred to as the heterogenization interval. The slow passage through the heterogenization interval leads to a finely dispersed separation of the T phase, the phase interfaces of the separated particles of the T phase forming preferred germ sites for the precipitation of Al 3 Zr particles starting at a temperature of about 350 ° C. When the ingot is heated further to the homogenization temperature, the previously separated particles of the T phase dissolve and what remains is an even distribution of the fine, submicron A ^ Zr precipitates, which are preferably due to the original particle boundaries of the T phase and to subcom boundaries and so that there is a homogeneous distribution. These fine Al 3 Zr particles cause a strong growth inhibition in the recrystallization of the plates in solution annealing as well as in the homogenization annealing of cast ingots, and the desired isotropic grain structure in the ingot results. The grain-refining additional element Zr is thus optimally used.
Ein weiteres wesentliches Merkmal des erfindungsgemässen Verfahrens ist die kombinierte Homogenisierungs- und Lösungsglühung mit anschliessender zweistufiger Abkühlung, wogegen bei den üblichen Verfahren nach dem Stand der Technik zur Erzielung einer auch in der Barrenmitte noch akzeptablen Festigkeit eine separate Lösungsglühung mit nachfolgendem Abschrecken bei hoher Abkühlungsgeschwindigkeit erforderlich ist.A further essential feature of the method according to the invention is the combined homogenization and solution annealing with subsequent two-stage cooling, whereas the usual methods according to the state of the art In order to achieve a strength that is still acceptable in the middle of the ingot, a separate solution annealing with subsequent quenching at a high cooling rate is required in the technology.
Unter dem Begriff "Abkühlen an bewegter Luft" bzw. "forced air cooling" wird hier eine üblicherweise durch Ventilatoren unterstützte Luftabkühlung verstanden, die zu einem Wärmeübergangskoeffizienten an der Barrenoberfläche von etwa 40 W/m2K führt. Das Abkühlen in einem Wasser/Luft-Sprühnebel führt zu einem etwas höheren Wärmeübergangskoeffizienten an der Barrenoberfläche.The term “cooling in moving air” or “forced air cooling” is understood here to mean an air cooling which is usually supported by fans and which leads to a heat transfer coefficient on the bar surface of approximately 40 W / m 2 K. Cooling in a water / air spray leads to a somewhat higher heat transfer coefficient on the bar surface.
Die erfindungsgemässe Legierung weist eine geringe Abschreckempfindlichkeit auf. Bei der Herstellung dicker Platten ist der Festigkeitsverlust im Plattenkern trotz der verhältnismässig milden Abkühlungsbedingungen kleiner als bei den Legierungen nach dem Stand der Technik. Es hat sich zudem überraschender- weise herausgestellt, dass dieser Effekt bei direkt aus Stranggussbarren gefertigten Platten noch viel ausgeprägter ist als bei warmgewalzten Platten.The alloy according to the invention has a low quench sensitivity. In the production of thick plates, the loss of strength in the plate core is smaller than in the prior art alloys, despite the relatively mild cooling conditions. Surprisingly, it has also been found that this effect is much more pronounced for plates made directly from continuous cast ingots than for hot-rolled plates.
Bei der Herstellung der dicken Platten hat sich die zweistufige Abkühlung von der Homogenisierungstemperatur auf Raumtemperatur als besonders vorteil- haft zur Erzielung einer Struktur mit geringen Eigenspannungen herausgestellt.In the manufacture of the thick plates, the two-stage cooling from the homogenization temperature to room temperature has proven to be particularly advantageous for achieving a structure with low residual stresses.
Zum Warmaushärten wird bevorzugt nacheinander eine Raumtemperaturlagerung, eine erste Wärmebehandlung bei einer ersten Temperatur und eine zweite Wärmebehandlung bei einer gegenüber der ersten Temperatur höheren zweiten Temperatur durchgeführt, z.B.For thermosetting, room temperature storage, a first heat treatment at a first temperature and a second heat treatment at a second temperature higher than the first temperature are preferably carried out in succession, e.g.
- 1 bis 30 Tage Lagerung bei Raumtemperatur,- 1 to 30 days storage at room temperature,
- 6 bis 10 h Lagerung bei einer Temperatur von 90 bis 100°C,- 6 to 10 h storage at a temperature of 90 to 100 ° C,
- 8 bis 22 h Lagerung bei einer Temperatur von 150 bis 160°C.- 8 to 22 h storage at a temperature of 150 to 160 ° C.
Besonders bevorzugt ist die Warmaushärtung zum Wärmebehandlungszustand Der Anwendungsbereich der erfindungsgemässen Legierung und der aus dieser hergestellten dicken Platten ergibt sich aus dem vorstehend beschriebenen Eigenschaftsspektrum. Die Platten eignen sich insbesondere für den Formenbau, d.h. für die Fertigung von Kunststoff-Spritzgiessformen, aber auch allge- mein für den Maschinen-, Werkzeug- und Formenbau.Heat curing to the heat treatment state is particularly preferred The field of application of the alloy according to the invention and of the thick plates produced therefrom results from the range of properties described above. The plates are particularly suitable for mold making, ie for the production of plastic injection molds, but also generally for machine, tool and mold making.
Weitere Vorteile, Merkmale und Einzelheiten der Erfindung ergeben sich aus der nachfolgenden Beschreibung bevorzugter Ausführungsbeispiele sowie anhand der Zeichnung; diese zeigt schematisch inFurther advantages, features and details of the invention result from the following description of preferred exemplary embodiments and from the drawing; this shows schematically in
- Fig. 1 die Verteilung der Brinell-Härte über einen Teil des Querschnitts eines Stranggussbarrens mit einem Querschnitt von 440 mm x 900 mm nach Ventilatorkühlung.- Fig. 1 shows the distribution of Brinell hardness over part of the cross section of a continuous casting ingot with a cross section of 440 mm x 900 mm after fan cooling.
- Fig. 2 den gemessenen Temperaturverlauf bei einem Stranggussbarren mit einem Querschnitt von 440 mm x 900 mm an der Oberfläche und in der Mitte bei Ventilatorkühlung;2 shows the measured temperature profile in the case of a continuous cast ingot with a cross section of 440 mm × 900 mm on the surface and in the middle with fan cooling;
- Fig. 3 den berechneten Verlauf der inneren Temperaturgradienten beim- Fig. 3 shows the calculated course of the internal temperature gradients at
Temperaturverlauf von Fig. 2;Temperature curve of Fig. 2;
- Fig. 4 den berechneten Temperaturverlauf bei einem Stranggussbarren mit einem Querschnitt von 1000 mm x 1200 mm an der Oberfläche und in der Mitte bei Ventilatorkühlung;4 shows the calculated temperature profile in the case of a continuous casting ingot with a cross section of 1000 mm × 1200 mm on the surface and in the middle with fan cooling;
- Fig. 5 den berechneten Verlauf der inneren Temperaturgradienten beim5 shows the calculated course of the internal temperature gradients at
Temperatuπterlauf von Fig. 4;Temperatuπterlauf of Fig. 4;
Beispielexample
Eine Legierung mit der Zusammensetzung (in Gew.-%): 0.040 Si, 0.08 Fe, 0.14 Cu, 0.0046 Mn, 2.69 Mg, 0.0028 Cr, 4.69 Zn, 0.017 Ti, 0.16 Zr, Rest AI, wurde in industriellem Massstab zu einem Stranggussbarren mit einem Querschnitt von 440 x 900 mm vergossen. Der Barren wurden innerhalb von 30 h auf eine Temperatur von 480°C aufgeheizt, wobei darauf geachtet wurde, dass die Auf- heizgeschwindigkeit im Bereich zwischen 170 und 410°C weniger als 20°C/h betrug. Die Homogenisierung des Barrens zum Ausgleich der erstarrungsbedingten Kristallseigerungen erfolgte durch Halten des Barrens während 12h bei 480°C.An alloy with the composition (in% by weight): 0.040 Si, 0.08 Fe, 0.14 Cu, 0.0046 Mn, 2.69 Mg, 0.0028 Cr, 4.69 Zn, 0.017 Ti, 0.16 Zr, balance AI, became an industrial ingot on an industrial scale cast with a cross section of 440 x 900 mm. The ingot was heated to a temperature of 480 ° C within 30 hours, taking care that the heating rate in the range between 170 and 410 ° C was less than 20 ° C / h. The ingot was homogenized to compensate for the solidification-induced crystal segregation by holding the ingot at 480 ° C. for 12 hours.
Der homogenisierte Barren wurden in einer ersten Stufe an ruhender Luft von der Homogenisierungstemperatur auf eine Zwischentemperatur von 400°C und anschliessend in einer zweiten Stufe mit Ventilatoren von 400°C auf 100°C abgekühlt. Die weitere Abkühlung auf Raumtemperatur erfolgte wiederum an ru- hender Luft.The homogenized ingot was cooled in a first stage in still air from the homogenization temperature to an intermediate temperature of 400 ° C and then in a second stage with fans from 400 ° C to 100 ° C. The further cooling to room temperature was again carried out in resting air.
Der Barren wurde nach 14 Tagen Lagerung bei Raumtemperatur während 8h bei 95°C und anschliessend während 18h bei 155°C zum überhärteten Zustand T76 warm ausgehärtet.After 14 days of storage at room temperature, the ingot was hot-cured at 95 ° C. for 8 hours and then at 155 ° C. for 18 hours to the over-hardened state T76.
An senkrecht zur Barrenlängsrichtung herausgesägten Proben der warmausgehärteten Barren wurde die Brinell-Härte über den Barrenquerschnitt bestimmt. Die in Fig. 1 dargestellten Bereiche gleicher Härte zeigen deutlich den geringen Härte- bzw. Festigkeitsverlust im Barrenkern gegenüber der Barrenoberfläche.The Brinell hardness was determined over the cross-section of the bar on samples of the thermally hardened ingot sawed out perpendicular to the longitudinal direction of the ingot. The areas of the same hardness shown in FIG. 1 clearly show the slight loss of hardness or strength in the bar core compared to the bar surface.
In Fig. 2 sind die für die Oberfläche (O) und den Kern (K) eines Barrens mit einem Querschnitt von 440 x 900 mm berechneten Temperatur-Zeit-Kurven bei einer Ventilatorabkühlung und in Fig. 3 die daraus abgeleiteten Gradienten zwischen der Temperatur T« im Barrenkern und der Temperatur To an der Bar- renoberfläche dargestellt. Zum Vergleich zeigen die Fig. 4 und 5 die entsprechenden Kurven für einen Barren mit einem Querschnitt von 1000 x 1200 mm. Die Ergebnisse zeigen, dass mit dem erfindungsgemässen Verfahren hergestellte Barren mit einer Dicke bis zu 1000 mm immer noch die an Platten zur Fertigung von Kunststoff-Spritzgiessformen bezüglich der mechanischen Festigkeit gestellten Anforderungen erfüllen dürften. 2 shows the temperature-time curves for a fan cooling for the surface (O) and the core (K) of an ingot with a cross section of 440 × 900 mm, and in FIG. 3 the gradients between the temperature T derived therefrom «In the bar core and the temperature To on the bar surface. For comparison, FIGS. 4 and 5 show the corresponding curves for an ingot with a cross section of 1000 x 1200 mm. The results show that bars produced with the method according to the invention with a thickness of up to 1000 mm are still likely to meet the mechanical strength requirements placed on plates for the production of plastic injection molds.
Claims
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP03789376A EP1587965B1 (en) | 2003-01-16 | 2003-12-20 | Aluminium alloy with increased resistance and low quench sensitivity |
| SI200330959T SI1587965T1 (en) | 2003-01-16 | 2003-12-20 | Aluminium alloy with increased resistance and low quench sensitivity |
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP03405013A EP1441041A1 (en) | 2003-01-16 | 2003-01-16 | Aluminium alloy with high strength and low quenching sensitivity |
| EP03405013 | 2003-01-16 | ||
| PCT/EP2003/014696 WO2004063407A1 (en) | 2003-01-16 | 2003-12-20 | Aluminium alloy with increased resistance and low quench sensitivity |
| EP03789376A EP1587965B1 (en) | 2003-01-16 | 2003-12-20 | Aluminium alloy with increased resistance and low quench sensitivity |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP1587965A1 true EP1587965A1 (en) | 2005-10-26 |
| EP1587965B1 EP1587965B1 (en) | 2007-07-18 |
Family
ID=32524285
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP03405013A Withdrawn EP1441041A1 (en) | 2003-01-16 | 2003-01-16 | Aluminium alloy with high strength and low quenching sensitivity |
| EP03789376A Expired - Lifetime EP1587965B1 (en) | 2003-01-16 | 2003-12-20 | Aluminium alloy with increased resistance and low quench sensitivity |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP03405013A Withdrawn EP1441041A1 (en) | 2003-01-16 | 2003-01-16 | Aluminium alloy with high strength and low quenching sensitivity |
Country Status (16)
| Country | Link |
|---|---|
| US (2) | US20060096676A1 (en) |
| EP (2) | EP1441041A1 (en) |
| AT (1) | ATE367456T1 (en) |
| AU (1) | AU2003293963A1 (en) |
| CA (1) | CA2513333C (en) |
| DE (1) | DE50307736D1 (en) |
| DK (1) | DK1587965T3 (en) |
| ES (1) | ES2290544T3 (en) |
| HR (1) | HRP20050704B1 (en) |
| NO (1) | NO340750B1 (en) |
| PL (1) | PL203780B1 (en) |
| PT (1) | PT1587965E (en) |
| RU (1) | RU2351674C2 (en) |
| SI (1) | SI1587965T1 (en) |
| TW (1) | TWI291993B (en) |
| WO (1) | WO2004063407A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012080592A1 (en) | 2010-12-14 | 2012-06-21 | Constellium France | Thick products made of 7xxx alloy and manufacturing process |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1683882B2 (en) | 2005-01-19 | 2010-07-21 | Otto Fuchs KG | Aluminium alloy with low quench sensitivity and process for the manufacture of a semi-finished product of this alloy |
| CN100363146C (en) * | 2005-05-20 | 2008-01-23 | 东北轻合金有限责任公司 | Manufacturing method of aluminum alloy profiles for pontoon bridges |
| WO2007135838A1 (en) | 2006-05-18 | 2007-11-29 | Kabushiki Kaisha Kobe Seiko Sho | Process for producing aluminum alloy plate and aluminum alloy plate |
| CN100523242C (en) * | 2006-11-13 | 2009-08-05 | 上海昊华模具有限公司 | Aluminium alloy for Vehicular radial ply tyre moulds |
| WO2009156283A1 (en) * | 2008-06-24 | 2009-12-30 | Aleris Aluminum Koblenz Gmbh | Al-zn-mg alloy product with reduced quench sensitivity |
| DE102008053893B4 (en) * | 2008-10-30 | 2010-08-19 | Audi Ag | Apparatus and method for cooling at least one cast component |
| RU2457422C2 (en) * | 2010-04-16 | 2012-07-27 | Российская Федерация в лице Министерства промышленности торговли Российской Федерации | Manufacturing method of sandwich plate based on aluminium for bullet-proof welded armour |
| RU2489217C1 (en) * | 2011-12-27 | 2013-08-10 | Открытое акционерное общество "Всероссийский институт легких сплавов" (ОАО "ВИЛС") | Method of sheets production from heat-hardened aluminium alloys alloyed with scandium and zirconium |
| JP6344923B2 (en) | 2014-01-29 | 2018-06-20 | 株式会社Uacj | High strength aluminum alloy and manufacturing method thereof |
| CA3032261A1 (en) | 2016-08-26 | 2018-03-01 | Shape Corp. | Warm forming process and apparatus for transverse bending of an extruded aluminum beam to warm form a vehicle structural component |
| EA037441B1 (en) * | 2016-09-30 | 2021-03-29 | Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" | Method for making deformed semi-finished products from aluminium alloys |
| EP3529394A4 (en) | 2016-10-24 | 2020-06-24 | Shape Corp. | Multi-stage aluminum alloy forming and thermal processing method for the production of vehicle components |
| CN112921220A (en) * | 2021-01-25 | 2021-06-08 | 西南铝业（集团）有限责任公司 | Al-Zn-Cu-Mg ingot and preparation method thereof |
Family Cites Families (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3542606A (en) * | 1968-03-13 | 1970-11-24 | Kaiser Aluminium Chem Corp | Hot worked metal article of aluminum base alloy and method of producing same |
| US3694272A (en) * | 1970-12-24 | 1972-09-26 | Kaiser Aluminium Chem Corp | Method for forming aluminum sheet |
| ATA113876A (en) * | 1976-02-18 | 1978-04-15 | Vmw Ranshofen Berndorf Ag | WELDABLE, EXTREMELY HOT FORMING, BORON-FREE CAST AND WET ALUMINUM ALLOYS WITH HIGH RESISTANCE AGAINST STRESS Cracks AND COATING CORROSION WITH AT THE SAME TIME GOOD MECHANICAL PROPERTIES |
| US4618382A (en) * | 1983-10-17 | 1986-10-21 | Kabushiki Kaisha Kobe Seiko Sho | Superplastic aluminium alloy sheets |
| JPH0794701B2 (en) * | 1991-04-01 | 1995-10-11 | 住友軽金属工業株式会社 | Manufacturing method of aluminum alloy soft material for welded structure |
| US5389165A (en) * | 1991-05-14 | 1995-02-14 | Reynolds Metals Company | Low density, high strength Al-Li alloy having high toughness at elevated temperatures |
| MX9204270A (en) * | 1991-07-23 | 1993-01-01 | Alcan Int Ltd | IMPROVED ALUMINUM ALLOY. |
| JPH07252573A (en) * | 1994-03-17 | 1995-10-03 | Kobe Steel Ltd | Al-zn-mg-cu alloy excellent in toughness and its production |
| US5961752A (en) * | 1994-04-07 | 1999-10-05 | Northwest Aluminum Company | High strength Mg-Si type aluminum alloy |
| RU2094516C1 (en) * | 1995-02-24 | 1997-10-27 | Акционерное общество "Самарская металлургическая компания" | Aluminium deformable thermally strengthened alloy |
| RU2094517C1 (en) * | 1995-02-24 | 1997-10-27 | Акционерное общество "Самарская металлургическая компания" | Aluminium deformable thermally strengthened alloy |
| RU2087582C1 (en) * | 1996-02-20 | 1997-08-20 | Галина Ивановна Медведева | Method of manufacturing parts from aluminium alloys |
| JP4204650B2 (en) | 1996-12-09 | 2009-01-07 | 三井金属鉱業株式会社 | High strength heat-resistant zinc alloy and molded product |
| JP3638188B2 (en) * | 1996-12-12 | 2005-04-13 | 住友軽金属工業株式会社 | Manufacturing method of high strength aluminum alloy extruded tube for front fork outer tube of motorcycle with excellent stress corrosion cracking resistance |
| WO2002063059A1 (en) * | 2000-10-20 | 2002-08-15 | Pechiney Rolled Products, Llc | High strenght aluminum alloy |
-
2003
- 2003-01-16 EP EP03405013A patent/EP1441041A1/en not_active Withdrawn
- 2003-12-20 PL PL376309A patent/PL203780B1/en not_active IP Right Cessation
- 2003-12-20 PT PT03789376T patent/PT1587965E/en unknown
- 2003-12-20 SI SI200330959T patent/SI1587965T1/en unknown
- 2003-12-20 ES ES03789376T patent/ES2290544T3/en not_active Expired - Lifetime
- 2003-12-20 CA CA2513333A patent/CA2513333C/en not_active Expired - Fee Related
- 2003-12-20 HR HR20050704A patent/HRP20050704B1/en not_active IP Right Cessation
- 2003-12-20 AT AT03789376T patent/ATE367456T1/en active
- 2003-12-20 RU RU2005125727/02A patent/RU2351674C2/en not_active IP Right Cessation
- 2003-12-20 AU AU2003293963A patent/AU2003293963A1/en not_active Abandoned
- 2003-12-20 US US10/541,788 patent/US20060096676A1/en not_active Abandoned
- 2003-12-20 EP EP03789376A patent/EP1587965B1/en not_active Expired - Lifetime
- 2003-12-20 DK DK03789376T patent/DK1587965T3/en active
- 2003-12-20 WO PCT/EP2003/014696 patent/WO2004063407A1/en not_active Ceased
- 2003-12-20 DE DE50307736T patent/DE50307736D1/en not_active Expired - Lifetime
- 2003-12-25 TW TW092136857A patent/TWI291993B/en not_active IP Right Cessation
-
2005
- 2005-08-15 NO NO20053832A patent/NO340750B1/en not_active IP Right Cessation
-
2009
- 2009-03-12 US US12/402,966 patent/US7901522B2/en not_active Expired - Fee Related
Non-Patent Citations (1)
| Title |
|---|
| See references of WO2004063407A1 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012080592A1 (en) | 2010-12-14 | 2012-06-21 | Constellium France | Thick products made of 7xxx alloy and manufacturing process |
Also Published As
| Publication number | Publication date |
|---|---|
| DK1587965T3 (en) | 2007-11-19 |
| DE50307736D1 (en) | 2007-08-30 |
| HRP20050704A2 (en) | 2006-02-28 |
| TWI291993B (en) | 2008-01-01 |
| TW200427850A (en) | 2004-12-16 |
| CA2513333A1 (en) | 2004-07-29 |
| PT1587965E (en) | 2007-10-12 |
| RU2351674C2 (en) | 2009-04-10 |
| WO2004063407A1 (en) | 2004-07-29 |
| SI1587965T1 (en) | 2007-12-31 |
| PL203780B1 (en) | 2009-11-30 |
| AU2003293963A1 (en) | 2004-08-10 |
| NO20053832L (en) | 2005-10-17 |
| ES2290544T3 (en) | 2008-02-16 |
| NO340750B1 (en) | 2017-06-12 |
| HRP20050704B1 (en) | 2008-06-30 |
| US20090223608A1 (en) | 2009-09-10 |
| ATE367456T1 (en) | 2007-08-15 |
| EP1441041A1 (en) | 2004-07-28 |
| RU2005125727A (en) | 2007-02-27 |
| US7901522B2 (en) | 2011-03-08 |
| CA2513333C (en) | 2010-09-14 |
| PL376309A1 (en) | 2005-12-27 |
| EP1587965B1 (en) | 2007-07-18 |
| NO20053832D0 (en) | 2005-08-15 |
| US20060096676A1 (en) | 2006-05-11 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| DE3689777T2 (en) | Multi-purpose, high conductivity, high strength copper alloys and process for their manufacture. | |
| DE2953182C2 (en) | Method for producing an alloy product from an aluminium alloy | |
| EP2829624B1 (en) | Aluminium material with improved precipitation hardening | |
| DE2817978C2 (en) | ||
| DE69737768T2 (en) | 6XXX ALUMINUM ALLOY | |
| DE69836569T3 (en) | Process for increasing the fracture toughness in aluminum-lithium alloys | |
| EP1587965B1 (en) | Aluminium alloy with increased resistance and low quench sensitivity | |
| DE69325804T2 (en) | HIGH-STRENGTH AL-LI ALLOY WITH LOW DENSITY AND HIGH TENSITY AT HIGH TEMPERATURES | |
| DE112008003052T5 (en) | Product of Al-Mg-Zn wrought alloy and manufacturing method therefor | |
| EP1682688A1 (en) | Al/mg/si cast aluminium alloy containing scandium | |
| DE202017007472U1 (en) | Systems for the manufacture of high-thickness aluminum alloy articles | |
| DE69618710T2 (en) | Method and device for the simplified production of a heat-treatable aluminum alloy | |
| DE60001249T2 (en) | Ti-Al (Mo, V, Si, Fe) alloys and process for their manufacture | |
| DE3852092T2 (en) | High-strength titanium material with improved ductility and process for producing this material. | |
| DE60023753T2 (en) | HEAT TREATMENT FOR AGING-HARDENING ALUMINUM ALLOYS | |
| DE2348248A1 (en) | METHOD OF TREATING A NICKEL BASE ALLOY | |
| DE3837544A1 (en) | METHOD FOR IMPROVING THE FRACTION QUALITY OF A HIGH-TIN TITANIUM ALLOY | |
| DE2647391A1 (en) | MANUFACTURE OF EXTRUDED PRODUCTS FROM ALUMINUM ALLOYS | |
| DE10163039C1 (en) | Hot and cold formable component made of an aluminum alloy and process for its production | |
| DE60114281T2 (en) | Cast and forged product using a copper-based alloy | |
| DE69614264T2 (en) | TREATMENT OF ALUMINUM ITEMS TO INCREASE BURN-TURNABILITY | |
| DE112017007033T5 (en) | ALUMINUM ALLOYS | |
| EP2061912B1 (en) | ALUMINIUM ALLOY OF THE AlZnMg TYPE AND METHOD OF PRODUCING IT | |
| EP0989195B1 (en) | Heat resisting aluminium alloy of the type AlCuMg | |
| DE69921146T2 (en) | METHOD FOR THE PRODUCTION OF HEAT-TREATABLE PANEL OBJECTS |
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 |
|
| 17P | Request for examination filed |
Effective date: 20050816 |
|
| AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR |
|
| AX | Request for extension of the european patent |
Extension state: AL LT LV MK |
|
| RIN1 | Information on inventor provided before grant (corrected) |
Inventor name: HOELLRIGL, GUENTHER Inventor name: JAQUEROD, CHRISTOPHE |
|
| DAX | Request for extension of the european patent (deleted) | ||
| GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
| RBV | Designated contracting states (corrected) |
Designated state(s): AT BE BG CH CZ DE DK ES FI FR GB GR HU IT LI LU MC NL PT RO SE SI SK TR |
|
| GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
| GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
| AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AT BE BG CH CZ DE DK ES FI FR GB GR HU IT LI LU MC NL PT RO SE SI SK TR |
|
| REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D Free format text: NOT ENGLISH |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
| REF | Corresponds to: |
Ref document number: 50307736 Country of ref document: DE Date of ref document: 20070830 Kind code of ref document: P |
|
| GBT | Gb: translation of ep patent filed (gb section 77(6)(a)/1977) |
Effective date: 20070815 |
|
| REG | Reference to a national code |
Ref country code: RO Ref legal event code: EPE |
|
| REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
| REG | Reference to a national code |
Ref country code: PT Ref legal event code: SC4A Free format text: AVAILABILITY OF NATIONAL TRANSLATION Effective date: 20071001 |
|
| ET | Fr: translation filed | ||
| REG | Reference to a national code |
Ref country code: GR Ref legal event code: EP Ref document number: 20070402961 Country of ref document: GR |
|
| REG | Reference to a national code |
Ref country code: DK Ref legal event code: T3 |
|
| REG | Reference to a national code |
Ref country code: HU Ref legal event code: AG4A Ref document number: E002077 Country of ref document: HU |
|
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2290544 Country of ref document: ES Kind code of ref document: T3 |
|
| PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
| STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
| 26N | No opposition filed |
Effective date: 20080421 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: MC Payment date: 20101201 Year of fee payment: 8 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BG Payment date: 20101215 Year of fee payment: 8 Ref country code: FI Payment date: 20101229 Year of fee payment: 8 Ref country code: LU Payment date: 20110103 Year of fee payment: 8 Ref country code: RO Payment date: 20101213 Year of fee payment: 8 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GR Payment date: 20101228 Year of fee payment: 8 Ref country code: SE Payment date: 20101229 Year of fee payment: 8 |
|
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: PC2A Owner name: ENGINEERED PRODUCTS SWITZERLAND AG Effective date: 20110907 |
|
| BECN | Be: change of holder's name |
Owner name: CONSTELLIUM SWITZERLAND A.G. Effective date: 20110906 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: PUE Owner name: CONSTELLIUM SWITZERLAND AG (LTD, SA) Free format text: ALCAN TECHNOLOGY & MANAGEMENT LTD.#BADISCHE BAHNHOFSTRASSE 16#8212 NEUHAUSEN AM RHEINFALL (CH) -TRANSFER TO- CONSTELLIUM SWITZERLAND AG (LTD, SA)#MAX HOEGGER-STRASSE 6#8048 ZUERICH (CH) Ref country code: CH Ref legal event code: NV Representative=s name: NOVAGRAAF SWITZERLAND SA |
|
| REG | Reference to a national code |
Ref country code: FR Ref legal event code: TP Owner name: ENGINEERED PRODUCTS SWITZERLAND AG, CH Effective date: 20111004 Ref country code: FR Ref legal event code: CD Owner name: ENGINEERED PRODUCTS SWITZERLAND AG, CH Effective date: 20111004 |
|
| REG | Reference to a national code |
Ref country code: NL Ref legal event code: SD Effective date: 20111214 Ref country code: NL Ref legal event code: TD Effective date: 20111214 |
|
| REG | Reference to a national code |
Ref country code: SI Ref legal event code: SP73 Owner name: CONSTELLIUM SWITZERLAND AG; CH Effective date: 20111103 Ref country code: FR Ref legal event code: CD Owner name: CONSTELLIUM SWITZERLAND AG, CH Effective date: 20111130 |
|
| REG | Reference to a national code |
Ref country code: SK Ref legal event code: TC4A Ref document number: E 2528 Country of ref document: SK Owner name: CONSTELLIUM SWITZERLAND AG, ZUERICH, CH Effective date: 20111212 Ref country code: SK Ref legal event code: PC4A Ref document number: E 2528 Country of ref document: SK Owner name: ALCAN FINANCES SWITZERLAND AG, ZUERICH, CH Free format text: FORMER OWNER: ALCAN TECHNOLOGY & MANAGEMENT LTD., NEUHAUSEN AM RHEINFALL, CH Effective date: 20111103 |
|
| REG | Reference to a national code |
Ref country code: PT Ref legal event code: PC4A Owner name: ALCAN FINANCES SWITZERLAND AG, CH Effective date: 20120118 |
|
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: PC2A Owner name: CONSTELLIUM SWITZERLAND AG Effective date: 20120228 |
|
| REG | Reference to a national code |
Ref country code: HU Ref legal event code: FH1C Free format text: FORMER REPRESENTATIVE(S): ERDELY PETER, DANUBIA SZABADALMI ES JOGI IRODA KFT., HU Representative=s name: DANUBIA SZABADALMI ES JOGI IRODA KFT., HU Ref country code: HU Ref legal event code: GB9C Owner name: CONSTELLIUM SWITZERLAND AG, CH Free format text: FORMER OWNER(S): ALCAN TECHNOLOGY & MANAGEMENT LTD., CH |
|
| REG | Reference to a national code |
Ref country code: DE Ref legal event code: R081 Ref document number: 50307736 Country of ref document: DE Owner name: CONSTELLIUM SWITZERLAND AG, CH Free format text: FORMER OWNER: ALCAN TECHNOLOGY & MANAGEMENT LTD., NEUHAUSEN AM RHEINFALL, CH Effective date: 20120319 |
|
| REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E Free format text: REGISTERED BETWEEN 20120510 AND 20120516 |
|
| REG | Reference to a national code |
Ref country code: AT Ref legal event code: PC Ref document number: 367456 Country of ref document: AT Kind code of ref document: T Owner name: CONSTELLIUM SWITZERLAND AG, CH Effective date: 20120420 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MC Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20111231 |
|
| REG | Reference to a national code |
Ref country code: SE Ref legal event code: EUG |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20111220 |
|
| REG | Reference to a national code |
Ref country code: GR Ref legal event code: ML Ref document number: 20070402961 Country of ref document: GR Effective date: 20120704 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RO Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20111220 Ref country code: SE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20111221 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20120704 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20111220 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BG Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20121231 |
|
| REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 13 |
|
| REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 14 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20151220 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: HU Payment date: 20161214 Year of fee payment: 14 Ref country code: DK Payment date: 20161227 Year of fee payment: 14 Ref country code: SK Payment date: 20161202 Year of fee payment: 14 Ref country code: NL Payment date: 20161226 Year of fee payment: 14 Ref country code: CH Payment date: 20161227 Year of fee payment: 14 Ref country code: GB Payment date: 20161228 Year of fee payment: 14 Ref country code: CZ Payment date: 20161208 Year of fee payment: 14 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20161227 Year of fee payment: 14 Ref country code: SI Payment date: 20161205 Year of fee payment: 14 Ref country code: AT Payment date: 20161202 Year of fee payment: 14 Ref country code: PT Payment date: 20161205 Year of fee payment: 14 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20161207 Year of fee payment: 14 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20151220 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IT Payment date: 20161222 Year of fee payment: 14 |
|
| PGRI | Patent reinstated in contracting state [announced from national office to epo] |
Ref country code: IT Effective date: 20170710 |
|
| REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 15 |
|
| REG | Reference to a national code |
Ref country code: DK Ref legal event code: EBP Effective date: 20171231 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CZ Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 Ref country code: PT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180620 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
| REG | Reference to a national code |
Ref country code: NL Ref legal event code: MM Effective date: 20180101 |
|
| REG | Reference to a national code |
Ref country code: AT Ref legal event code: MM01 Ref document number: 367456 Country of ref document: AT Kind code of ref document: T Effective date: 20171220 |
|
| GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20171220 |
|
| REG | Reference to a national code |
Ref country code: SK Ref legal event code: MM4A Ref document number: E 2528 Country of ref document: SK Effective date: 20171220 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180101 |
|
| REG | Reference to a national code |
Ref country code: SI Ref legal event code: KO00 Effective date: 20180806 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 Ref country code: HU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171221 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SK Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171231 Ref country code: AT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 Ref country code: SI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171221 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171231 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171231 |
|
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20190703 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: ES Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171221 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20171220 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20221227 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20221227 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20221228 Year of fee payment: 20 |
|
| REG | Reference to a national code |
Ref country code: DE Ref legal event code: R071 Ref document number: 50307736 Country of ref document: DE |
|
| REG | Reference to a national code |
Ref country code: BE Ref legal event code: MK Effective date: 20231220 |