EP0989195A1 - Heat resisting aluminium alloy of the type AlCuMg - Google Patents

Heat resisting aluminium alloy of the type AlCuMg Download PDF

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Publication number
EP0989195A1
EP0989195A1 EP98810967A EP98810967A EP0989195A1 EP 0989195 A1 EP0989195 A1 EP 0989195A1 EP 98810967 A EP98810967 A EP 98810967A EP 98810967 A EP98810967 A EP 98810967A EP 0989195 A1 EP0989195 A1 EP 0989195A1
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Prior art keywords
weight
aluminum alloy
plate
max
alloy according
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EP98810967A
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German (de)
French (fr)
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EP0989195B1 (en
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Günther Höllrigl
Christophe Jaquerod
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3A Composites International AG
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Alcan Technology and Management Ltd
Alusuisse Lonza Services Ltd
Alusuisse Technology and Management Ltd
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Application filed by Alcan Technology and Management Ltd, Alusuisse Lonza Services Ltd, Alusuisse Technology and Management Ltd filed Critical Alcan Technology and Management Ltd
Priority to PT98810967T priority Critical patent/PT989195E/en
Priority to ES98810967T priority patent/ES2175647T3/en
Priority to AT98810967T priority patent/ATE216737T1/en
Priority to EP98810967A priority patent/EP0989195B1/en
Priority to DE59803924T priority patent/DE59803924D1/en
Publication of EP0989195A1 publication Critical patent/EP0989195A1/en
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    • 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
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium

Definitions

  • the invention relates to an aluminum alloy of the AlCuMg condition high mechanical strength and high heat resistance, which are used in the solution-annealed quenched, stretched and aged a yield stress at room temperature of Rp0.2> 450 MPa, after a pre-storage of 300 h at 160 ° C a yield stress at 160 ° C of Rp0.2> 340 MPa and after a creep load of 1000 h at 160 ° C below a tensile stress of 260 MPa has an elongation of less than 0.5%.
  • AlCuMg alloys with high mechanical strength and high heat resistance have in practice especially the alloy AA2618 and, due to its good weldability, the alloy AA2219 enforced.
  • a newer alloy of type AA2618 with good Heat resistance is known from EP-A-0756014.
  • the invention has for its object an alloy of the type AlCuMg of the type mentioned with a compared to the known alloys to create increased thermal stability according to the prior art.
  • the alloy for the production of plastic molds i.e. Injection molds for injection molding plastic, at operating temperatures up to about 160 ° C.
  • the preferred copper content is 5.2 to 5.4% by weight.
  • the maximum solubility for copper in this alloy is around 5.2 to 5.3% Cu.
  • Part of the copper is absorbed in the primary intermetallic phases AlFeMnCu, which makes it possible to practically reach the solubility limit.
  • the primary eutectic phase Al 2 Cu forms in the structure, which does not contribute to the strength, but as a local cathodic element, however, reduces the corrosion resistance of the alloy.
  • the alloy according to the invention preferably lies mainly in the phase field of the ⁇ '-precipitation hardening, with the equilibrium phase Al 2 Cu. If the magnesium content rises above 0.6%, there are corresponding proportions of S'-precipitation hardening with the equilibrium phase Al 2 CuMg.
  • the positive effect of a silver additive on precipitation hardening is preferably effective in ⁇ '-precipitation hardening because the silver can form the ⁇ phase together with the magnesium on the (111) lattice planes of the aluminum matrix, which leads to an additional increase in strength . With even higher magnesium contents, the excretion of the ⁇ phase is superimposed by the S 'excretion and reduces the strength-increasing effect of silver.
  • an alloy with higher magnesium contents is sensitive to the speed of the quenching treatment, which leads to a loss of strength in the middle of thick plates.
  • an optimum between achievable strength at room temperature and at elevated temperatures is achieved.
  • the alloy according to the invention is therefore particularly suitable for the production of thick plates.
  • the alloy can be used to further increase strength Contain 0.05 to 0.5 wt .-%, preferably 0.3 to 0.5 wt .-% silver.
  • an isotropic distribution of the internal stresses in the cross section of the plates produced by hot rolling is to be aimed for.
  • the grain size and the grain shape in the plate are of importance for the reduction of the internal stresses.
  • the finer and more uniform the crystal thaw after the recrystallization with the solution annealing preferably carried out in the range from 510 to 525 ° C., 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.
  • a fine grain structure can be achieved in the hot-rolled plate by controlling the heat treatment and the hot rolling temperatures in such a way that the distribution of submicron precipitates of Al 3 Zr in the structure is as homogeneous as possible.
  • the homogenized cast ingots can either be cooled from the homogenization temperature to the holding or hot rolling temperature or heated up to this temperature range.
  • a heterogenization occurs with the elimination of the equilibrium phase Al 2 Cu.
  • the phase interfaces of the Al 2 Cu particles are formed as preferred nucleation sites for the Al 3 Zr precipitates.
  • the hot-rolled plate is subsequently heated to the solution annealing temperature, the Al 2 Cu particles dissolve and what remains is a uniform distribution of the fine, submicron Al 3 Zr precipitates, which are preferably due to the original Al 2 Cu particle boundaries and to sub-grain boundaries and thus one result in homogeneous distribution.
  • These fine Al 3 Zr particles cause a strong growth inhibition during recrystallization during solution treatment and the desired isotropic grain structure results in the plate.
  • the sum of iron and silicon has also proven to be expedient and the sum of zirconium and titanium each to max. 0.25% by weight limit.
  • the preferred content range for manganese is 0.2 to 0.4% by weight.
  • the alloy which is particularly suitable for the production of Plastic molds are suitable, starting from a casting block without kneading operations are further processed, however, the manufacturing process usually includes at least one kneading step. If it is the dimensions of a Allow shape to be produced are preferred as the starting material hot-rolled plates used. In certain cases it can also turn out to be prove expedient, for example a decrease in thickness in a first Direction by hot rolling and in a second direction by forging to create. In particular for the production of inexpensive forms for The production of mass parts can also be extrusion as a processing step be considered. The extrusion process opens up basically also the possibility of certain contours of a later form already preform.
  • Alloys A and B are according to the invention, alloys AA2618 and AA 2219 serve as reference alloys or reference materials.
  • Alloys A and B were used as continuous cast ingots on an industrial scale poured.
  • the homogenization of the cast ingots to compensate for the solidification Crystal segregation was carried out according to the usual procedure for AlCuMg alloys.
  • the ingots cooled after the homogenization annealing were raised to 410 ° C heated, held at this temperature for 3 h and then starting rolled from this temperature to a plate thickness of 70 mm. Subsequently the plates were at a temperature of 520 ° C solution annealed and subsequently in water using a defined convective Heat transfer quenched so that the resulting residual stresses were controllable by the subsequent stretching operation. The stretched Plates were then at a temperature of 180 ° C during Cured warm for 12 hours.
  • the yield stresses Rp 0.2 were determined after 300 h and 500 h pre-storage at a temperature of 160 ° C by tensile tests at room temperature (RT) and at 160 ° C on samples of the thermoset plates and on samples of the reference materials taken from commercially available plates. The results are shown in Tables 2 and 3.
  • the plates used as reference materials had a thickness of 20 mm in the case of alloy AA2618 and a thickness of 90 mm in the case of alloy AA2219.
  • the creep data were determined on round specimens with a measuring length of 160 mm. Out the strain-time diagram in Fig. 1 are the results for the four examined Alloys visible.
  • the load applied to the test bars was 260 MPa, the test temperature was set to 160 ° C.
  • the curves show clearly the improved heat resistance compared to the comparative alloys the alloy according to the invention.

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  • Chemical & Material Sciences (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Metal Rolling (AREA)
  • Conductive Materials (AREA)
  • Shaping By String And By Release Of Stress In Plastics And The Like (AREA)
  • Heat Treatment Of Articles (AREA)
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  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)
  • Insulated Conductors (AREA)

Abstract

Aluminum alloy of the AlCuMg type contains alloying additions (in wt.%) of 4.5-5.5 Cu, 0.45-0.65 Mg, maximum 0.2 Si, maximum 0,25 Fe, maximum 0.8 Mn, maximum 0.15 Ti, and optionally 0.12-0.25 Zr, 0.05-0.5 Ag and maximum 0.15 impurities. An Independent claim is also included for the manufacture of a plate made of Al alloy comprising casting an ingot of the alloy, homogenizing the cast ingot, maintaining the ingot at 380-440 degrees C for at least 2.5 hours, hot rolling the ingot to a plate at 380-440 degrees C, solution annealing the plate, quenching, stretching the plate by 1-5%, and hardening the plate.

Description

Die Erfindung betrifft eine Aluminiumlegierung vom Typ AlCuMg Zustand mit hoher mechanischer Festigkeit und hoher Wärmebeständigkeit, die im lösungsgeglühten, abgeschreckten, gestreckten und warmausgelagerten Zustand eine Fliessspannung bei Raumtemperatur von Rp0.2 > 450 MPa, nach einer Vorlagerung von 300 h bei 160°C eine Fliessspannung bei 160°C von Rp0.2 > 340 MPa und nach einer Kriechbelastung von 1000 h bei 160°C unter einer Zugspannung von 260 MPa eine Dehnung von weniger als 0.5% aufweist.The invention relates to an aluminum alloy of the AlCuMg condition high mechanical strength and high heat resistance, which are used in the solution-annealed quenched, stretched and aged a yield stress at room temperature of Rp0.2> 450 MPa, after a pre-storage of 300 h at 160 ° C a yield stress at 160 ° C of Rp0.2> 340 MPa and after a creep load of 1000 h at 160 ° C below a tensile stress of 260 MPa has an elongation of less than 0.5%.

Zur Herstellung von Kunststoffbauteilen durch Spritzgiesstechnik werden heute Betriebstemperaturen bis gegen 160°C angewendet. Für den Formenbau werden hochfeste Aluminiumlegierungen eingesetzt, welche ihre Festigkeit durch Ausscheidungshärtung erhalten. Die erwähnten Betriebstemperaturen von ca. 160°C erreichen jedoch den Überhärtungsbereich der aushärtbaren hochfesten Werkstoffe vom Typ AlZnMgCu. Für den Einsatz bei erhöhten Temperaturen sind deshalb AlCu- und AlCuMg-Legierungen besser geeignet, um ein hohes Festigkeitsniveau bei diesen erhöhten Betriebstemperaturen über einen langen Zeitraum zu erhalten.For the production of plastic components by injection molding technology today Operating temperatures up to 160 ° C applied. For mold making high-strength aluminum alloys are used, which are characterized by their strength Precipitation hardening received. The mentioned operating temperatures of approx. However, 160 ° C reach the over-hardening range of the hardenable high-strength AlZnMgCu type materials. For use at elevated temperatures therefore AlCu and AlCuMg alloys are better suited to a high Strength level at these elevated operating temperatures over a long period Period.

Als Legierungen vom Typ AlCuMg mit gleichzeitig hoher mechanischer Festigkeit und hoher Wärmebeständigkeit haben sich in der Praxis vor allem die Legierung AA2618 und, wegen ihrer guten Schweissbarkeit, die Legierung AA2219 durchgesetzt. Eine neuere Legierung vom Typ AA2618 mit guter Warmfestigkeit ist aus EP-A-0756014 bekannt.As AlCuMg alloys with high mechanical strength and high heat resistance have in practice especially the alloy AA2618 and, due to its good weldability, the alloy AA2219 enforced. A newer alloy of type AA2618 with good Heat resistance is known from EP-A-0756014.

Der Erfindung liegt die Aufgabe zugrunde, eine Legierung vom Typ AlCuMg der eingangs genannten Art mit einer gegenüber den bekannten Legierungen nach dem Stand der Technik erhöhten thermischen Stabilität zu schaffen. Insbesondere soll die Legierung zur Herstellung von Kunststoffformen, d.h. Spritzgiessformen zum Spritzgiessen von Kunststoff, bei Betriebstemperaturen bis zu etwa 160°C geeignet sein.The invention has for its object an alloy of the type AlCuMg of the type mentioned with a compared to the known alloys to create increased thermal stability according to the prior art. In particular is the alloy for the production of plastic molds, i.e. Injection molds for injection molding plastic, at operating temperatures up to about 160 ° C.

Zur erfindungsgemässen Lösung der Aufgabe führt, dass die Legierung

  • 4.5 bis 5.5 Gew.-% Kupfer
  • 0.45 bis 0.65 Gew.-% Magnesium
  • max. 0.2 Gew.-% Silizium
  • max. 0.25 Gew.-% Eisen
  • max. 0.8 Gew.-% Mangan
  • max. 0.15 Gew.-% Titan
    wahlweise noch
  • 0.12 bis 0.25 Gew.-% Zirkonium
  • 0.05 bis 0.5 Gew.-% Silber
    sowie Aluminium als Rest mit herstellungsbedingten Verunreinigungen einzeln max. 0.05 Gew.-%, insgesamt max. 0.15 Gew.-% enthält.
    • The achievement of the object according to the invention is that the alloy
  • 4.5 to 5.5% by weight copper
  • 0.45 to 0.65% by weight of magnesium
  • Max. 0.2% by weight silicon
  • Max. 0.25% by weight iron
  • Max. 0.8% by weight of manganese
  • Max. 0.15% by weight titanium
    optionally still
  • 0.12 to 0.25% by weight of zirconium
  • 0.05 to 0.5 wt% silver
    and aluminum as the rest with manufacturing-related impurities individually max. 0.05% by weight, total max. Contains 0.15% by weight.

    • Es hat sich gezeigt, dass die erfindungsgemässe Legierung gegenüber den AlCuMg-Legierungen nach dem Stand der Technik eine geringere Abschreckempfindlichkeit aufweist, was dazu führt, dass bei der Herstellung dicker Platten der Festigkeitsverlust in der Plattenmitte kleiner ist.It has been shown that the alloy according to the invention compared to the AlCuMg alloys according to the prior art have a lower quench sensitivity has, which results in the production of thick plates the loss of strength in the middle of the panel is smaller.

    Zur Erzielung einer möglichst hohen Festigkeit bei gleichzeitig guter Korrosionsbeständigkeit beträgt der bevorzugte Kupfergehalt 5.2 bis 5.4 Gew.-%.To achieve the highest possible strength with good corrosion resistance the preferred copper content is 5.2 to 5.4% by weight.

    Die maximale Löslichkeit für Kupfer liegt bei dieser Legierung bei etwa 5.2 bis 5.3% Cu. Ein Teil des Kupfers wird in den primären intermetallischen Phasen AlFeMnCu absorbiert, was es überhaupt ermöglicht, praktisch an die Löslichkeitsgrenze zu gehen. Bei höheren Kupfergehalten entsteht im Gefüge die primäre eutektische Phase Al2Cu, die keinen Beitrag an die Festigkeit leistet, als kathodisches Lokalelement jedoch den Korrosionswiderstand der Legierung herabsetzt.The maximum solubility for copper in this alloy is around 5.2 to 5.3% Cu. Part of the copper is absorbed in the primary intermetallic phases AlFeMnCu, which makes it possible to practically reach the solubility limit. At higher copper contents, the primary eutectic phase Al 2 Cu forms in the structure, which does not contribute to the strength, but as a local cathodic element, however, reduces the corrosion resistance of the alloy.

    Bevorzugt liegt die erfindungsgemässe Legierung hauptsächlich im Phasenfeld der '-Ausscheidungshärtung, mit der Gleichgewichtsphase Al2Cu. Steigt der Magnesiumgehalt über 0.6%, so ergeben sich entsprechend Anteile von S'-Ausscheidungshärtung, mit der Gleichgewichtsphase Al2CuMg. Der positive Effekt eines Silberzusatzes auf die Ausscheidungshärtung ist jedoch bei der '-Ausscheidungshärtung bevorzugt wirksam, weil das Silber zusammen mit dem Magnesium die Ω-Phase bilden kann, und zwar auf den (111) Gitterebenen der Aluminiummatrix, was zu einem zusätzlichen Festigkeitsanstieg führt. Bei noch höheren Magnesiumgehalten wird die Ausscheidung der Ω-Phase von der S'-Ausscheidung überlagert und setzt die festigkeitssteigernde Wirkung von Silber herab. Hinzu kommt, dass eine Legierung mit höheren Magnesiumgehalten empfindlich auf die Geschwindigkeit der Abschreckbehandlung reagiert, was zu einem Festigkeitsverlust in der Mitte von dicken Platten führt. Mit der erfindungsgemässen Beschränkung des Magnesiumgehaltes wird ein Optimum zwischen erzielbarer Festigkeit bei Raumtemperatur und bei erhöhten Temperaturen erreicht. Die erfindungsgemässe Legierung eignet sich daher insbesondere zur Herstellung dicker Platten.The alloy according to the invention preferably lies mainly in the phase field of the '-precipitation hardening, with the equilibrium phase Al 2 Cu. If the magnesium content rises above 0.6%, there are corresponding proportions of S'-precipitation hardening with the equilibrium phase Al 2 CuMg. However, the positive effect of a silver additive on precipitation hardening is preferably effective in '-precipitation hardening because the silver can form the Ω phase together with the magnesium on the (111) lattice planes of the aluminum matrix, which leads to an additional increase in strength . With even higher magnesium contents, the excretion of the Ω phase is superimposed by the S 'excretion and reduces the strength-increasing effect of silver. In addition, an alloy with higher magnesium contents is sensitive to the speed of the quenching treatment, which leads to a loss of strength in the middle of thick plates. With the limitation of the magnesium content according to the invention, an optimum between achievable strength at room temperature and at elevated temperatures is achieved. The alloy according to the invention is therefore particularly suitable for the production of thick plates.

    Wie vorstehend erwähnt, kann zur weiteren Steigerung der Festigkeit die Legierung 0.05 bis 0.5 Gew.-%, vorzugsweise 0.3 bis 0.5 Gew.-% Silber enthalten.As mentioned above, the alloy can be used to further increase strength Contain 0.05 to 0.5 wt .-%, preferably 0.3 to 0.5 wt .-% silver.

    Insbesondere für die Anwendung der erfindungsgemässen Legierung als Werkstoff für den Formenbau ist eine möglichst isotrope Verteilung der Eigenspannungen im Querschnitt der durch Warmwalzen gefertigten Platten anzustreben. Für den Abbau der Eigenspannungen ist u.a. die Korngrösse und die Kornform in der Platte von Bedeutung. Je feiner und gleichmässiger die Kristaue nach der Rekristallisation bei der vorzugsweise im Bereich von 510 bis 525°C durchgeführten Lösungsglühung 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. Durch einen Zusatz von 0.12 bis 0.25 Gew.-% Zirkonium kann ein feines Korngefüge in der warmgewalzten Platte erreicht werden, indem man die Wärmebehandlung und die Warmwalztemperaturen so steuert, dass eine möglichst homogene Verteilung von submikronen Ausscheidungen von Al3Zr im Gefüge entsteht.In particular for the use of the alloy according to the invention as a material for mold construction, an isotropic distribution of the internal stresses in the cross section of the plates produced by hot rolling is to be aimed for. The grain size and the grain shape in the plate are of importance for the reduction of the internal stresses. The finer and more uniform the crystal thaw after the recrystallization with the solution annealing preferably carried out in the range from 510 to 525 ° C., 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. By adding 0.12 to 0.25% by weight of zirconium, a fine grain structure can be achieved in the hot-rolled plate by controlling the heat treatment and the hot rolling temperatures in such a way that the distribution of submicron precipitates of Al 3 Zr in the structure is as homogeneous as possible.

    Die erfindungsgemässe Herstellung einer Platte ist gekennzeichnet durch die Schritte

    • Giessen eines Barrens aus der Legierung,
    • Homogenisieren des gegossenen Barrens,
    • Halten des Barrens während mindestens 2.5 h in einem Temperaturbereich von 380 bis 440°C,
    • Warmwalzen des Barrens zur Platte im Temperaturbereich von 380 bis 440°C,
    • Lösungsglühen der Platte,
    • Abschrecken der Platte,
    • Strecken der Platte um 1 bis 5%, und
    • Warmaushärten der Platte.
    The production of a plate according to the invention is characterized by the steps
    • Casting an ingot from the alloy,
    • Homogenizing the cast ingot,
    • Keeping the ingot in a temperature range of 380 to 440 ° C for at least 2.5 h,
    • Hot rolling of the ingot to the plate in the temperature range from 380 to 440 ° C,
    • Solution annealing of the plate,
    • Quenching the plate,
    • Stretch the plate by 1 to 5%, and
    • Heat cure the plate.

    Die homogenisierten Gussbarren können entweder von der Homogenisierungstemperatur auf die Halte- bzw. Warmwalztemperatur abgekühlt oder in diesen Temperaturbereich aufgeheizt werden. Beim Halten des Barrens im Temperaturbereich von 380 bis 440°C tritt mit der Ausscheidung der Gleichgewichtsphase Al2Cu eine Heterogenisierung ein. Beim anschliessenden Warmwalzen in demselben Temperaturbereich werden die Phasengrenzflächen der Al2Cu-Teilchen als bevorzugte Keimstellen für die Al3Zr-Ausscheidungen gebildet. Beim darauffolgenden Aufheizen der Warmwalzplatte auf die Lösungsglühtemperatur lösen sich die Al2Cu-Teilchen auf und zurück bleibt eine gleichmässige Verteilung der feinen, submikronen Al3Zr-Ausscheidungen, welche bevorzugt an den ursprünglichen Al2Cu-Teilchengrenzen sowie an Subkorngrenzen liegen und damit eine homogene Verteilung ergeben. Diese feinen Al3Zr-Teilchen bewirken eine starke Wachstumshemmung bei der Rekristallisation während der Lösungsglühung und es resultiert das gewünschte isotrope Korngefüge in der Platte.The homogenized cast ingots can either be cooled from the homogenization temperature to the holding or hot rolling temperature or heated up to this temperature range. When the ingot is kept in the temperature range from 380 to 440 ° C, a heterogenization occurs with the elimination of the equilibrium phase Al 2 Cu. During the subsequent hot rolling in the same temperature range, the phase interfaces of the Al 2 Cu particles are formed as preferred nucleation sites for the Al 3 Zr precipitates. When the hot-rolled plate is subsequently heated to the solution annealing temperature, the Al 2 Cu particles dissolve and what remains is a uniform distribution of the fine, submicron Al 3 Zr precipitates, which are preferably due to the original Al 2 Cu particle boundaries and to sub-grain boundaries and thus one result in homogeneous distribution. These fine Al 3 Zr particles cause a strong growth inhibition during recrystallization during solution treatment and the desired isotropic grain structure results in the plate.

    Weiter hat sich als zweckmässig herausgestellt, die Summe von Eisen und Silizium und die Summe von Zirkonium und Titan je auf max. 0.25 Gew.-% zu begrenzen.The sum of iron and silicon has also proven to be expedient and the sum of zirconium and titanium each to max. 0.25% by weight limit.

    Der bevorzugte Gehaltsbereich für Mangan liegt bei 0.2 bis 0.4 Gew.-%.The preferred content range for manganese is 0.2 to 0.4% by weight.

    Grundsätzlich kann die Legierung, die sich insbesondere zur Herstellung von Kunststoffformen eignet, ausgehend von einem Gussblock ohne Knetoperationen weiterverarbeitet werden, jedoch beinhaltet das Herstellungsverfahren üblicherweise mindestens einen Knetschritt. Sofern es die Dimensionen einer herzustellenden Form zulassen, werden als Ausgangsmaterial bevorzugt warmgewalzte Platten eingesetzt. In gewissen Fällen kann es sich auch als zweckmässig erweisen, eine Dickenabnahme beispielsweise in einer ersten Richtung durch Warmwalzen und in einer zweiten Richtung durch Schmieden zu erzeugen. Insbesondere zur Herstellung von kostengünstigen Formen für die Produktion von Massenteilen kann auch Strangpressen als Verarbeitungsschritt in Betracht gezogen werden. Mit dem Strangpressen eröffnet sich grundsätzlich auch die Möglichkeit, gewisse Konturen einer späteren Form bereits vorzuformen.Basically, the alloy, which is particularly suitable for the production of Plastic molds are suitable, starting from a casting block without kneading operations are further processed, however, the manufacturing process usually includes at least one kneading step. If it is the dimensions of a Allow shape to be produced are preferred as the starting material hot-rolled plates used. In certain cases it can also turn out to be prove expedient, for example a decrease in thickness in a first Direction by hot rolling and in a second direction by forging to create. In particular for the production of inexpensive forms for The production of mass parts can also be extrusion as a processing step be considered. The extrusion process opens up basically also the possibility of certain contours of a later form already preform.

    Weitere Vorteile, Merkmale und Einzelheiten der Erfindung ergeben sich aus der nachfolgenden Beschreibung bevorzugter Ausführungsbeispiele sowie anhand der Zeichnung; diese zeigt schematisch in

    - Fig. 1
    Dehnungs-Zeit Diagramm von erfindungsgemässen Legierungen im Vergleich zu Legierungen nach dem Stand der Technik.
    Further 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
    Strain-time diagram of alloys according to the invention compared to alloys according to the prior art.

    BeispieleExamples

    Die chemischen Analysen der untersuchten Legierungen sind aus der Tabelle 1 ersichtlich. Die Legierungen A und B sind erfindungsgemäss, die Legierungen AA2618 und AA 2219 dienen als Vergleichslegierungen bzw. Referenzwerkstoffe. Leg. Zusammensetzung [Gew.-%] Si Fe Cu Mn Mg Ag Ti V Zr Ni A 0.10 0.14 5.25 0.30 0.60 0.38 0.08 -- 0.18 -- B 0.10 0.14 5.30 0.30 0.60 -- -- 0.09 0.20 -- AA2618 0.15 1.05 2.60 -- 1.65 -- 0.06 -- -- 1.10 AA2219 0.06 0.06 6.11 0.31 0.02 -- 0.04 0.08 0.12 -- The chemical analyzes of the alloys examined are shown in Table 1. Alloys A and B are according to the invention, alloys AA2618 and AA 2219 serve as reference alloys or reference materials. Leg. Composition [% by weight] Si Fe Cu Mn Mg Ag Ti V Zr Ni A 0.10 0.14 5.25 0.30 0.60 0.38 0.08 - 0.18 - B 0.10 0.14 5.30 0.30 0.60 - - 0.09 0.20 - AA2618 0.15 1.05 2.60 - 1.65 - 0.06 - - 1.10 AA2219 0.06 0.06 6.11 0.31 0.02 - 0.04 0.08 0.12 -

    Die Legierungen A und B wurden als Stranggussbarren in industriellem Massstab gegossen. Die Homogenisierung der Gussbarren zum Ausgleich der erstarrungsbedingten Kristallseigerungen erfolgte nach der üblichen Vorschrift für AlCuMg-Legierungen.Alloys A and B were used as continuous cast ingots on an industrial scale poured. The homogenization of the cast ingots to compensate for the solidification Crystal segregation was carried out according to the usual procedure for AlCuMg alloys.

    Die nach der Homogenisierungsglühung abgekühlten Barren wurden auf 410°C aufgeheizt, 3 h bei dieser Temperatur gehalten und nachfolgend ausgehend von dieser Temperatur auf eine Plattendicke von 70 mm gewalzt. Anschliessend wurden die Platten während 40 min bei einer Temperatur von 520°C lösungsgeglüht und nachfolgend in Wasser mittels definierter konvektiver Wärmeübertragung so abgeschreckt, dass die entstehenden Eigenspannungen durch die nachfolgende Streckoperation kontrollierbar waren. Die gestreckten Platten wurden anschliessend bei einer Temperatur von 180°C während 12 h warm ausgehärtet.The ingots cooled after the homogenization annealing were raised to 410 ° C heated, held at this temperature for 3 h and then starting rolled from this temperature to a plate thickness of 70 mm. Subsequently the plates were at a temperature of 520 ° C solution annealed and subsequently in water using a defined convective Heat transfer quenched so that the resulting residual stresses were controllable by the subsequent stretching operation. The stretched Plates were then at a temperature of 180 ° C during Cured warm for 12 hours.

    An Proben der warmausgehärteten Platten sowie an aus kommerziell erhältlichen Platten entnommenen Proben der Referenzwerkstoffe wurden die Fliessspannungen Rp 0.2 nach 300 h und 500 h Vorlagerung bei einer Temperatur von 160°C durch Zugversuche bei Raumtemperatur (RT) und bei 160°C ermittelt. Die Ergebnisse sind in den Tabellen 2 und 3 dargestellt. Die als Referenzwerkstoffe verwendeten Platten wiesen im Falle der Legierung AA2618 eine Dicke von 20 mm und bei der Legierung AA2219 eine Dicke von 90 mm auf. Legierung Zugversuch bei RT (20°C) Rp0.2 [MPa] nach 300 h Rp0.2 [MPa] nach 500 h A 432 405 B 407 390 AA2618 418 -- AA2219 340 335 Legierung Zugversuch bei 160°C Rp0.2 [MPa] nach 300 h Rp0.2 [MPa] nach 500 h A 370 350 B 342 332 AA2618 350 -- AA2219 281 270 The yield stresses Rp 0.2 were determined after 300 h and 500 h pre-storage at a temperature of 160 ° C by tensile tests at room temperature (RT) and at 160 ° C on samples of the thermoset plates and on samples of the reference materials taken from commercially available plates. The results are shown in Tables 2 and 3. The plates used as reference materials had a thickness of 20 mm in the case of alloy AA2618 and a thickness of 90 mm in the case of alloy AA2219. alloy Tensile test at RT (20 ° C) Rp0.2 [MPa] after 300 h Rp0.2 [MPa] after 500 h A 432 405 B 407 390 AA2618 418 - AA2219 340 335 alloy Tensile test at 160 ° C Rp0.2 [MPa] after 300 h Rp0.2 [MPa] after 500 h A 370 350 B 342 332 AA2618 350 - AA2219 281 270

    Die Kriechdaten wurden an Rundproben mit 160 mm Messlänge ermittelt. Aus dem Dehnungs-Zeit Diagramm in Fig. 1 sind die Ergebnisse für die vier untersuchten Legierungen ersichtlich. Die an die Probestäbe angelegte Last betrug 260 MPa, die Prüftemperatur wurde auf 160°C eingestellt. Die Kurven zeigen deutlich die gegenüber den Vergleichslegierungen verbesserte Warmfestigkeit der erfindungsgemässen Legierung.The creep data were determined on round specimens with a measuring length of 160 mm. Out the strain-time diagram in Fig. 1 are the results for the four examined Alloys visible. The load applied to the test bars was 260 MPa, the test temperature was set to 160 ° C. The curves show clearly the improved heat resistance compared to the comparative alloys the alloy according to the invention.

    Claims (12)

    Aluminiumlegierung vom Typ AlCuMg mit hoher mechanischer Festigkeit und hoher Wärmebeständigkeit, die im lösungsgeglühten, abgeschreckten, gestreckten und warmausgelagerten Zustand (T8) eine Fliessspannung bei Raumtemperatur von Rp0.2 > 450 MPa, nach einer Vorlagerung von 300 h bei 160°C eine Fliessspannung bei 160°C von Rp0.2 > 340 MPa und nach einer Kriechbelastung von 1000 h bei 160°C unter einer Zugspannung von 260 MPa eine Dehnung von weniger als 0.5% aufweist,
    dadurch gekennzeichnet, dass die Legierung 4.5 bis 5.5 Gew.-% Kupfer 0.45 bis 0.65 Gew.-% Magnesium max. 0.2 Gew.-% Silizium max. 0.25 Gew.-% Eisen max. 0.8 Gew.-% Mangan max. 0.15 Gew.-% Titan
    wahlweise noch     0.12 bis 0.25 Gew.-% Zirkonium 0.05 bis 0.5 Gew.-% Silber
    sowie Aluminium als Rest mit herstellungsbedingten Verunreinigungen einzeln max. 0.05 Gew.-%, insgesamt max. 0.15 Gew.-% enthält.         Aluminum alloy of the type AlCuMg with high mechanical strength and high heat resistance, which in solution annealed, quenched, stretched and heat aged (T8) a yield stress at room temperature of Rp0.2> 450 MPa, after a preliminary storage of 300 h at 160 ° C a yield stress 160 ° C of Rp0.2> 340 MPa and after a creep load of 1000 h at 160 ° C under a tensile stress of 260 MPa has an elongation of less than 0.5%,
    characterized in that the alloy 4.5 to 5.5% by weight copper 0.45 to 0.65% by weight of magnesium Max. 0.2% by weight silicon Max. 0.25% by weight iron Max. 0.8% by weight of manganese Max. 0.15% by weight titanium
    optionally still     0.12 to 0.25% by weight of zirconium 0.05 to 0.5 wt% silver
    and aluminum as the rest with manufacturing-related impurities individually max. 0.05% by weight, total max. Contains 0.15% by weight.     Aluminiumlegierung nach Anspruch 1, dadurch gekennzeichnet, dass sie 5.2 bis 5.4 Gew.-% Kupfer enthält.Aluminum alloy according to claim 1, characterized in that it Contains 5.2 to 5.4 wt .-% copper. Aluminiumlegierung nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass sie 0.3 bis 0.5 Gew.-% Silber enthält.Aluminum alloy according to claim 1 or 2, characterized in that that it contains 0.3 to 0.5% by weight of silver. Aluminiumlegierung nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Summe von Eisen und Silizium max. 0.25 Gew.-% beträgt.Aluminum alloy according to one of claims 1 to 3, characterized in that that the sum of iron and silicon max. Is 0.25% by weight. Aluminiumlegierung nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass die Summe von Zirkonium und Titan max. 0.25 Gew.-% beträgt.Aluminum alloy according to one of claims 1 to 4, characterized in that that the sum of zirconium and titanium max. 0.25% by weight is. Aluminiumlegierung nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass sie 0.2 bis 0.4 Gew.-% Mangan enthält.Aluminum alloy according to one of claims 1 to 5, characterized in that that it contains 0.2 to 0.4% by weight of manganese. Aluminiumlegierung nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass sie im gekneteten Zustand vorliegt.Aluminum alloy according to one of claims 1 to 6, characterized in that that it is kneaded. Aluminiumlegierung nach Anspruch 7, dadurch gekennzeichnet, dass der geknetete Zustand durch Warmwalzen erzeugt worden ist.Aluminum alloy according to claim 7, characterized in that the kneaded state has been generated by hot rolling. Aluminiumlegierung nach Anspruch 7, dadurch gekennzeichnet, dass der geknetete Zustand durch Schmieden erzeugt worden ist.Aluminum alloy according to claim 7, characterized in that the kneaded state has been produced by forging. Aluminiumlegierung nach Anspruch 7, dadurch gekennzeichnet, dass der geknetete Zustand durch Strangpressen erzeugt worden ist.Aluminum alloy according to claim 7, characterized in that the kneaded state has been generated by extrusion. Verfahren zur Herstellung einer Platte aus einer Aluminiumlegierung nach einem der Ansprüche 1 bis 6, gekennzeichnet durch die Schritte (a) Giessen eines Barrens aus der Legierung, (b) Homogenisieren des gegossenen Barrens, (c) Halten des Barrens während mindestens 2.5 h in einem Temperaturbereich von 380 bis 440°C, (d) Warmwalzen des Barrens zur Platte im Temperaturbereich von 380 bis 440°C, (e) Lösungsglühen der Platte, (f) Abschrecken der Platte, (g) Strecken der Platte um 1 bis 5%, und (h) Warmaushärten der Platte. A method of manufacturing an aluminum alloy plate according to any one of claims 1 to 6, characterized by the steps (a) casting an ingot from the alloy, (b) homogenizing the cast ingot, (c) keeping the ingot in a temperature range of 380 to 440 ° C for at least 2.5 h, (d) hot rolling the ingot to the plate in the temperature range from 380 to 440 ° C, (e) solution annealing of the plate, (f) quenching the plate, (g) stretching the plate 1 to 5%, and (h) thermosetting the plate. Verwendung einer Aluminiumlegierung nach einem der Ansprüche 1 bis 10 oder einer Platte hergestellt mit dem Verfahren nach Anspruch 11 zur Herstellung von Kunststoffformen.Use of an aluminum alloy according to one of claims 1 to 10 or a plate made with the method of claim 11 for Manufacture of plastic molds.
    EP98810967A 1998-09-25 1998-09-25 Heat resisting aluminium alloy of the type AlCuMg Revoked EP0989195B1 (en)

    Priority Applications (5)

    Application Number Priority Date Filing Date Title
    PT98810967T PT989195E (en) 1998-09-25 1998-09-25 ALUMINUM ALLOY LEATHER RESISTANT TO THE HEAT OF THE TIGO ALCUMG
    ES98810967T ES2175647T3 (en) 1998-09-25 1998-09-25 ALUMINUM ALLOY RESISTANT TO THE HEAT OF THE ALCUMG TYPE.
    AT98810967T ATE216737T1 (en) 1998-09-25 1998-09-25 HEAT-RESISTANT ALUMINUM ALLOY OF THE ALCUMG TYPE
    EP98810967A EP0989195B1 (en) 1998-09-25 1998-09-25 Heat resisting aluminium alloy of the type AlCuMg
    DE59803924T DE59803924D1 (en) 1998-09-25 1998-09-25 Heat-resistant aluminum alloy of the type AlCuMg

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    EP98810967A EP0989195B1 (en) 1998-09-25 1998-09-25 Heat resisting aluminium alloy of the type AlCuMg

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    EP0989195A1 true EP0989195A1 (en) 2000-03-29
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    Cited By (12)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    WO2004018721A1 (en) * 2002-08-20 2004-03-04 Corus Aluminium Walzprodukte Gmbh Al-Cu ALLOY WITH HIGH TOUGHNESS
    US6777106B2 (en) 2001-04-24 2004-08-17 Pechiney Rhenalu Metal blocks suitable for machining applications
    WO2008003503A2 (en) * 2006-07-07 2008-01-10 Aleris Aluminum Koblenz Gmbh Method of manufacturing aa2000 - series aluminium alloy products
    US7323068B2 (en) 2002-08-20 2008-01-29 Aleris Aluminum Koblenz Gmbh High damage tolerant Al-Cu alloy
    CN100469928C (en) * 2007-03-30 2009-03-18 中南大学 Prepn of high strength heat resistant aluminium alloy and its pipe
    US7604704B2 (en) 2002-08-20 2009-10-20 Aleris Aluminum Koblenz Gmbh Balanced Al-Cu-Mg-Si alloy product
    US8043445B2 (en) 2003-06-06 2011-10-25 Aleris Aluminum Koblenz Gmbh High-damage tolerant alloy product in particular for aerospace applications
    CN105274408A (en) * 2015-10-15 2016-01-27 东北轻合金有限责任公司 Manufacturing method of aluminum alloy rivet wire for aerospace
    CN109825749A (en) * 2019-04-10 2019-05-31 上海裕纪金属制品有限公司 One kind can punching press aluminium alloy extrusions heat-and corrosion-resistant heat treatment method and aluminium alloy extrusions
    CN109898000A (en) * 2019-03-29 2019-06-18 郑州轻研合金科技有限公司 A kind of super high strength heat resistant alloy and preparation method thereof
    US10472707B2 (en) 2003-04-10 2019-11-12 Aleris Rolled Products Germany Gmbh Al—Zn—Mg—Cu alloy with improved damage tolerance-strength combination properties
    CN115874031A (en) * 2022-12-07 2023-03-31 东北轻合金有限责任公司 Machining method of 2A12 aluminum alloy plate for aviation

    Families Citing this family (1)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    US7883591B2 (en) 2004-10-05 2011-02-08 Aleris Aluminum Koblenz Gmbh High-strength, high toughness Al-Zn alloy product and method for producing such product

    Citations (7)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    EP0224016A1 (en) * 1985-10-31 1987-06-03 BBC Brown Boveri AG Wrought aluminium alloy of the type Al-Cu-Mg having a high strength in the temperature range between 0 and 250o C
    WO1995027091A1 (en) * 1994-03-30 1995-10-12 Reynolds Metals Company Method of producing aluminum alloy extrusions
    WO1996029440A1 (en) * 1995-03-21 1996-09-26 Kaiser Aluminum & Chemical Corporation A method of manufacturing aluminum aircraft sheet
    EP0756017A1 (en) * 1995-07-28 1997-01-29 Pechiney Rhenalu Aluminium-copper-magnesium alloy with high creep resistance
    US5630889A (en) * 1995-03-22 1997-05-20 Aluminum Company Of America Vanadium-free aluminum alloy suitable for extruded aerospace products
    US5652063A (en) * 1995-03-22 1997-07-29 Aluminum Company Of America Sheet or plate product made from a substantially vanadium-free aluminum alloy
    US5800927A (en) * 1995-03-22 1998-09-01 Aluminum Company Of America Vanadium-free, lithium-free, aluminum alloy suitable for sheet and plate aerospace products

    Patent Citations (7)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    EP0224016A1 (en) * 1985-10-31 1987-06-03 BBC Brown Boveri AG Wrought aluminium alloy of the type Al-Cu-Mg having a high strength in the temperature range between 0 and 250o C
    WO1995027091A1 (en) * 1994-03-30 1995-10-12 Reynolds Metals Company Method of producing aluminum alloy extrusions
    WO1996029440A1 (en) * 1995-03-21 1996-09-26 Kaiser Aluminum & Chemical Corporation A method of manufacturing aluminum aircraft sheet
    US5630889A (en) * 1995-03-22 1997-05-20 Aluminum Company Of America Vanadium-free aluminum alloy suitable for extruded aerospace products
    US5652063A (en) * 1995-03-22 1997-07-29 Aluminum Company Of America Sheet or plate product made from a substantially vanadium-free aluminum alloy
    US5800927A (en) * 1995-03-22 1998-09-01 Aluminum Company Of America Vanadium-free, lithium-free, aluminum alloy suitable for sheet and plate aerospace products
    EP0756017A1 (en) * 1995-07-28 1997-01-29 Pechiney Rhenalu Aluminium-copper-magnesium alloy with high creep resistance

    Non-Patent Citations (2)

    * Cited by examiner, † Cited by third party
    Title
    ANYALEBECHI P N ET AL: "EFFECT OF SUPEREUTECTIC HOMOGENIZATION ON INCIDENCE OF POROSITY IN ALUMINUM ALLOY 2014 INGOT", METALLURGICAL AND MATERIALS TRANSACTIONS B: PROCESS METALLURGY & MATERIALS PROCESSING SCIENCE, vol. 25B, no. 1, 1 February 1994 (1994-02-01), pages 111 - 122, XP000425868 *
    M.J.HAYNES AND R.P.GANGLOFF: "ELEVATED TEMPERATURE FRACTURE TOUGHNESS OF Al-Cu-Mg-Ag SHEET: CHARACTERIZATION AND MODELING", METALLURGICAL AND MATERIALS TRANSACTIONS, vol. 28A, no. 9, pages 1815 - 1829, XP002087749 *

    Cited By (21)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    US6777106B2 (en) 2001-04-24 2004-08-17 Pechiney Rhenalu Metal blocks suitable for machining applications
    GB2406578A (en) * 2002-08-20 2005-04-06 Corus Aluminium Walzprod Gmbh Al-Cu Alloy with high toughness
    GB2406578B (en) * 2002-08-20 2006-04-26 Corus Aluminium Walzprod Gmbh Al-Cu alloy with high toughness
    CN1325682C (en) * 2002-08-20 2007-07-11 克里斯铝轧制品有限公司 Al-cu alloy with high toughness
    WO2004018721A1 (en) * 2002-08-20 2004-03-04 Corus Aluminium Walzprodukte Gmbh Al-Cu ALLOY WITH HIGH TOUGHNESS
    US7323068B2 (en) 2002-08-20 2008-01-29 Aleris Aluminum Koblenz Gmbh High damage tolerant Al-Cu alloy
    US7494552B2 (en) 2002-08-20 2009-02-24 Aleris Aluminum Koblenz Gmbh Al-Cu alloy with high toughness
    US7604704B2 (en) 2002-08-20 2009-10-20 Aleris Aluminum Koblenz Gmbh Balanced Al-Cu-Mg-Si alloy product
    US7815758B2 (en) 2002-08-20 2010-10-19 Aleris Aluminum Koblenz Gmbh High damage tolerant Al-Cu alloy
    US10472707B2 (en) 2003-04-10 2019-11-12 Aleris Rolled Products Germany Gmbh Al—Zn—Mg—Cu alloy with improved damage tolerance-strength combination properties
    US8043445B2 (en) 2003-06-06 2011-10-25 Aleris Aluminum Koblenz Gmbh High-damage tolerant alloy product in particular for aerospace applications
    DE112004000995B4 (en) 2003-06-06 2021-12-16 Corus Aluminium Walzprodukte Gmbh Highly damage tolerant aluminum alloy product, especially for aerospace applications
    WO2008003503A2 (en) * 2006-07-07 2008-01-10 Aleris Aluminum Koblenz Gmbh Method of manufacturing aa2000 - series aluminium alloy products
    RU2443798C2 (en) * 2006-07-07 2012-02-27 Алерис Алюминум Кобленц Гмбх Manufacturing methods of products from aluminium alloys of aa2000 series
    WO2008003503A3 (en) * 2006-07-07 2008-02-21 Aleris Aluminum Koblenz Gmbh Method of manufacturing aa2000 - series aluminium alloy products
    CN100469928C (en) * 2007-03-30 2009-03-18 中南大学 Prepn of high strength heat resistant aluminium alloy and its pipe
    CN105274408A (en) * 2015-10-15 2016-01-27 东北轻合金有限责任公司 Manufacturing method of aluminum alloy rivet wire for aerospace
    CN109898000A (en) * 2019-03-29 2019-06-18 郑州轻研合金科技有限公司 A kind of super high strength heat resistant alloy and preparation method thereof
    CN109825749A (en) * 2019-04-10 2019-05-31 上海裕纪金属制品有限公司 One kind can punching press aluminium alloy extrusions heat-and corrosion-resistant heat treatment method and aluminium alloy extrusions
    CN115874031A (en) * 2022-12-07 2023-03-31 东北轻合金有限责任公司 Machining method of 2A12 aluminum alloy plate for aviation
    CN115874031B (en) * 2022-12-07 2023-08-15 东北轻合金有限责任公司 Processing method of 2A12 aluminum alloy plate for aviation

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    ATE216737T1 (en) 2002-05-15

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