EP0845542A1 - Process of manufacturing semi-finished products in aluminium - Google Patents
Process of manufacturing semi-finished products in aluminium Download PDFInfo
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- EP0845542A1 EP0845542A1 EP97110712A EP97110712A EP0845542A1 EP 0845542 A1 EP0845542 A1 EP 0845542A1 EP 97110712 A EP97110712 A EP 97110712A EP 97110712 A EP97110712 A EP 97110712A EP 0845542 A1 EP0845542 A1 EP 0845542A1
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- semi
- melt
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
Definitions
- the present invention relates to a method for Manufacture of workpieces or semi-finished products from one low wear aluminum alloy with intermetallic Phase forming additives.
- Precipitation crystals have a grain size of significantly less than 80 ⁇ m, in the preferred case less than 20 ⁇ m.
- the present invention is therefore based on the object to create a method of the type described above with which also makes thick-walled, voluminous workpieces or semi-finished products a low-wear aluminum alloy in the casting process can be produced that are of high quality.
- the process is also intended to manufacture semi-finished products enable themselves in a subsequent forming process Have workpieces formed without having to Inhomogeneities the positive properties of the cast material get lost.
- This task is carried out in a method of the type mentioned solved according to the invention in that in a first step a melt of the alloy in such a small dimension is shed that such a high cooling rate is achieved that the precipitating crystals that form of the intermetallic phases homogeneously distributed and with defined grain size are excreted from the melt; that the primary material obtained in the first step Temperatures in the area of the heterogeneous area between Aluminum melt and intermetallic phase heated and that Aluminum is melted so far that the alloy is under Gravity is fluid and then that one Workpiece or a semi-finished product with compared to the dimension of the Primary material of larger dimensions is created.
- the melt becomes very high according to the invention cooled quickly so that a homogeneous distribution of the excreting intermetallic phases or Precipitation crystals is reached. While due to Diffusion processes with very slow solidification processes inside a thick-walled casting Precipitation crystals measuring 80 ⁇ m and above can have, according to the invention by rapid Cooling down a fine-grained homogeneous distribution of the Precipitation crystals "frozen". This is according to the Invention achieved in that the melt in the first Step is shed with a small dimension, which in Depends on the available cooling capacity is less than 50 mm, preferably less than 20 mm.
- the melt can be technically realized in a continuous casting "finger thick" or in pigs or tapes, especially also be cast on a casting wheel.
- the grain size should be less than 80 ⁇ m, preferably less than 40 ⁇ m and particularly are preferably less than 20 microns.
- the best Results are achieved when the dimension or Cooling rate is so high that grain sizes of less than 5 ⁇ m result.
- intermetallic phases are preferably aluminides, but in principle it could also be compounds of the alloying elements.
- the alloying elements for forming aluminides as intermetallic phases are preferably titanium and zircon which crystallize out to form Al 3 Ti and Al 3 Zr. If titanium is added, the remelting temperature in the second step of the method according to the invention is about 800 ° Celsius.
- the aluminum matrix is already liquid again, but the titanium aluminide, Al 3 Ti, with a melting point of 1460 ° Celsius is still solid. Due to the low solubility of the Al 3 Ti in the aluminum melt of about 0.4%, the precipitation crystals are largely preserved and are not dissolved.
- the temperature to which the starting material is reheated in the second step of the process according to the invention must be kept well below the melting temperature of the intermetallic phase in question, but on the other hand it must be so high that a sufficient proportion of melt for the subsequent shaping into the desired dimensions is available.
- the subsequent shaping or reshaping can be done by simple gravity casting but also in pressure or centrifugal casting.
- the semi-finished products with larger dimensions produced in this way are particularly suitable for forming, for example, in the extrusion process, forging, rolling or tixocasting, since the fine-grained, hard precipitation crystals are not destroyed during the forming processes and the wear-reducing phases are evenly distributed.
- Additives such as copper, magnesium, manganese can be added be used, which is the matrix hardness of the alloy increase. It can also prove advantageous if other hard crystals, e.g. Silicon into which Aluminum matrix can be stored.
- the micrograph according to FIG. 1 shows a fine-grained, homogeneous structure of a low-wear aluminum alloy, titanium and other additives increasing the matrix hardness being added.
- the dark phases represent precipitation crystals.
- a strand in the order of magnitude of approx. 20 mm diameter was cast and thereby solidified so quickly that precipitation crystals in the form of titanium aluminide, Al 3 Ti, homogeneously distributed with a dimension of less than 80 microns.
- the desired grain size is set via the strand dimensions and the heat dissipation conditions.
- the approximately "finger-thick" continuous casting is then brought back to a temperature of approximately 800 ° Celsius in a second process step, at which the aluminum matrix of the primary material is at least partially melted, so that a sufficient amount of melt for molding or casting a workpiece is compared the dimension of the finger-thick strand of the primary material of larger dimensions or for casting a semi-finished product, such as a thick rug, for a subsequent extrusion process.
- the remelting temperature in the second step of the process is clearly below the melting temperature of the titanium aluminide and, furthermore, the solubility of the titanium aluminide in the aluminum melt at the remelting temperature is only 0.4%, the fine-grained precipitates of the titanium aluminide are largely retained and also characterize the structure of the final workpiece or semi-finished product.
Abstract
Description
Die vorliegende Erfindung betrifft ein Verfahren zum Herstellen von Werkstücken oder Halbzeugen aus einer verschleißarmen Aluminium-Legierung mit intermetallische Phasen bildenden Zusätzen.The present invention relates to a method for Manufacture of workpieces or semi-finished products from one low wear aluminum alloy with intermetallic Phase forming additives.
Die Herstellung von Werkstücken oder Halbzeugen aus einer verschleißarmen Aluminium-Legierung im Gießverfahren war seither qualitativ hochstehend nur bei dünnwandigen Werkstücken oder Halbzeugen möglich. Bei dickwandigen Werkstücken oder Halbzeugen mit größeren Abmessungen ergibt sich zwangsläufig eine sehr langsame Erstarrungsgeschwindigkeit mit der Folge, dass sich im inneren eines voluminösen Gußstücks sehr große Ausscheidungskristalle der intermetallischen Phasen ausbilden. Dies beeinträchtigt die Qualität des Gußstücks durch die homogene Gefügeausbildung. Handelt es sich bei dem Gußstück um ein Halbzeugprodukt, so werden diese großen Ausscheidungskristalle bei der nachfolgenden Umformung, etwa im Strangpress oder Walzprozess, gebrochen bzw. zerstört, was zu einer erheblichen Verringerung der Festigkeit des Werkstoffs führt.The production of workpieces or semi-finished products from one low-wear aluminum alloy in the casting process since then high quality only for thin-walled Workpieces or semi-finished products possible. With thick-walled Workpieces or semi-finished products with larger dimensions inevitably a very slow one Solidification speed with the consequence that it is inside of a voluminous casting, very large precipitation crystals the intermetallic phases. This affects the quality of the casting through the homogeneous Microstructure. Is the casting a Semi-finished product, this is how these large precipitation crystals become in the subsequent forming, for example in the extrusion or Rolling process, broken or destroyed, resulting in a significant Reduction in the strength of the material leads.
Es war also bislang nicht möglich, bei der Herstellung dickwandiger Werkstücke oder Halbzeuge eine gleichmäßige sehr feinkörnige Ausscheidung von intermetallischen Hartphasen zu erreichen, wobei unter einer feinkörnigen Verteilung eine solche verstanden werden soll, bei der die Ausscheidungskristalle eine Korngröße von deutlich weniger als 80 µm, im bevorzugten Fall weniger als 20 µm aufweisen.So far it has not been possible to manufacture thick-walled workpieces or semi-finished products a very uniform fine-grained excretion of intermetallic hard phases achieve, with a fine-grained distribution is to be understood in which the Precipitation crystals have a grain size of significantly less than 80 µm, in the preferred case less than 20 µm.
Es ist zwar bekannt, verhältnismäßig dickwandige Werkstücke durch eine sogenannte Sprühkompaktierung mit möglichst feinkörnigen Ausscheidungskristallen herzustellen. Dabei wird unter Verwendung einer aufwendigen unter Schutzgasatmosphäre arbeitenden Apparatur ein Strahl aus flüssiger Aluminium-Schmelze zerstäubt und auf einen entsprechenden Zielkörper aufgesprüht, bis das gewünschte Werkstück quasi Schicht für Schicht aufgebaut wurde. Die Durchführung des Verfahrens ist kompliziert, sehr teuer und mit einem hohem Gefahrenpotential verbunden. Although it is known, relatively thick-walled workpieces by means of a so-called spray compaction, if possible to produce fine-grained precipitation crystals. Doing so using an elaborate under protective gas atmosphere working equipment a jet of liquid aluminum melt atomized and onto a corresponding target body sprayed on until the desired workpiece is quasi layer for Layer was built up. The procedure is complicated, very expensive and with a high risk potential connected.
Der vorliegenden Erfindung liegt daher die Aufgabe zugrunde ein Verfahren der eingangs beschriebenen Art zu schaffen, mit dem auch dickwandige, voluminöse Werkstücke oder Halbzeuge aus einer verschleißarmen Aluminium-Legierung im Gießverfahren hergestellt werden können, die qualitativ hochstehend sind. Das Verfahren soll ferner die Herstellung von Halbzeugen ermöglichen, die sich in einem nachfolgenden Umformprozess zu Werkstücken formen lassen, ohne dass dabei durch Inhomogenitäten die positiven Eigenschaften des Gußwerkstoffs verloren gehen.The present invention is therefore based on the object to create a method of the type described above with which also makes thick-walled, voluminous workpieces or semi-finished products a low-wear aluminum alloy in the casting process can be produced that are of high quality. The process is also intended to manufacture semi-finished products enable themselves in a subsequent forming process Have workpieces formed without having to Inhomogeneities the positive properties of the cast material get lost.
Diese Aufgabe wird bei einem Verfahren der genannten Art erfindungsgemäß dadurch gelöst, dass in einem ersten Schritt eine Schmelze der Legierung in derart geringer Abmessung vergossen wird, dass eine so hohe Abkühlungsgeschwindigkeit erreicht wird, dass die sich bildenden Ausscheidungskristalle der intermetallischen Phasen homogen verteilt und mit definierter Korngröße aus der Schmelze ausgeschieden werden; dass das im ersten Schritt erhaltene Vormaterial auf Temperaturen im Bereich des heterogenen Gebietes zwischen Aluminium-Schmelze und intermetallischer Phase erhitzt und das Aluminium soweit aufgeschmolzen wird, dass die Legierung unter Schwerkraftbedingungen fließfähig ist und dass dann ein Werkstück oder ein Halbzeug mit gegenüber der Abmessung des Vormaterials größerer Abmessung erstellt wird. This task is carried out in a method of the type mentioned solved according to the invention in that in a first step a melt of the alloy in such a small dimension is shed that such a high cooling rate is achieved that the precipitating crystals that form of the intermetallic phases homogeneously distributed and with defined grain size are excreted from the melt; that the primary material obtained in the first step Temperatures in the area of the heterogeneous area between Aluminum melt and intermetallic phase heated and that Aluminum is melted so far that the alloy is under Gravity is fluid and then that one Workpiece or a semi-finished product with compared to the dimension of the Primary material of larger dimensions is created.
In dem ersten Schritt wird die Schmelze erfindungsgemäß sehr rasch abgekühlt, damit eine homogene Verteilung der sich ausscheidenden intermetallischen Phasen bzw. Ausscheidungskristalle erreicht wird. Während aufgrund von Diffussionsprozessen bei sehr langsamen Erstarrungsprozessen im inneren eines dickwandigen Gußstücks die Ausscheidungskristalle eine Abmessung von 80 µm und darüber aufweisen können, wird gemäß der Erfindung durch rasches Abkühlen eine feinkörnige homogene Verteilung der Ausscheidungskristalle "eingefroren". Dies wird gemäß der Erfindung dadurch erreicht, dass die Schmelze in dem ersten Schritt mit einer geringen Abmessung vergossen wird, die in Abhängigkeit von der zur Verfügung stehenden Kühlkapazität geringer als 50 mm, vorzugsweise geringer als 20 mm ist. Zur technischen Verwirklichung kann die Schmelze im Strangguß "fingerdick" oder in Masseln oder Bändern, insbesondere auch über ein Gießrad vergossen werden. Auf diese Weise gelingt es, die intermetallischen Phasen in definierter Korngröße auszubilden. Die Korngröße soll in jedem Fall weniger als 80 µm, bevorzugtermaßen weniger als 40 µm und besonders bevorzugtermaßen weniger als 20 µm betragen. Die besten Ergebnisse werden erzielt, wenn die Abmessung bzw. die Abkühlungsgeschwindigkeit derart hoch ist, dass Korngrößen von weniger als 5 µm resultieren.In the first step, the melt becomes very high according to the invention cooled quickly so that a homogeneous distribution of the excreting intermetallic phases or Precipitation crystals is reached. While due to Diffusion processes with very slow solidification processes inside a thick-walled casting Precipitation crystals measuring 80 µm and above can have, according to the invention by rapid Cooling down a fine-grained homogeneous distribution of the Precipitation crystals "frozen". This is according to the Invention achieved in that the melt in the first Step is shed with a small dimension, which in Depends on the available cooling capacity is less than 50 mm, preferably less than 20 mm. For The melt can be technically realized in a continuous casting "finger thick" or in pigs or tapes, especially also be cast on a casting wheel. In this way, the intermetallic phases in a defined grain size to train. In any case, the grain size should be less than 80 µm, preferably less than 40 µm and particularly are preferably less than 20 microns. The best Results are achieved when the dimension or Cooling rate is so high that grain sizes of less than 5 µm result.
Zur Herstellung der Werkstücke oder Halbzeuge größerer Abmessung wird nun auf erfindungsgemäße Weise das im ersten Schritt erhaltene Vormaterial erneut auf Temperaturen erwärmt, bei denen die Aluminium-Matrix wenigstens teilweise bzw. soweit erschmolzen wird, die Ausscheidungskristalle der intermetallischen Phasen jedoch im Wesentlichen fest bleiben. Es wird dann ein Werkstück oder ein Halbzeug mit gegenüber der Abmessung des Vormaterials größerer Abmessung geformt, ohne dass die Ausscheidungskristalle ihre Feinkörnigkeit verlieren. Sie liegen also sowohl in dem Vormaterial als auch im fertigen Werkstück oder Halbzeug in derselben homogenen und feinkörnigen Verteilung vor. Ein auf diese erfindungsgemäße Weise hergestelltes Halbzeug kann dann einem Strangpressprozess oder einem Walzprozess unterworfen werden, ohne dass die Ausscheidungskristalle der intermetallischen Phasen zerstört werden. Dies ist auf ihre Feinkörnigkeit zurückzuführen.For the production of workpieces or semi-finished products larger Dimension is now the first in the manner according to the invention The material obtained in the step is again heated to temperatures, in which the aluminum matrix is at least partially or as far as is melted, the precipitation crystals of the intermetallic phases, however, remain essentially solid. It is then a workpiece or a semi-finished product with opposite Dimension of the raw material of larger dimension shaped without that the precipitation crystals lose their fine grain. So they are both in the primary material and in the finished one Workpiece or semi-finished product in the same homogeneous and fine-grained distribution. One according to this invention Semi-finished products produced in this way can then be Be subjected to an extrusion process or a rolling process, without the precipitation crystals of the intermetallic Phases are destroyed. This is due to their fine grain attributed.
Bei der Auswahl des die intermetallische Phasen bildenden Zusatzes oder der Zusätze erweist es sich als vorteilhaft, solche Legierungselemente zu wählen, welche intermetallische Phasen bilden,deren Schmelztemperatur möglichst hoch und deren Löslichkeit in der wieder aufgeschmolzenen Aluminium-Schmelze möglichst gering ist. Bei den intermetallischen Phasen handelt es sich bevorzugtermaßen um Aluminide, es könnten aber grundsätzlich auch Verbindungen der Legierungselemente sein. Bei den Legierungselementen zur Ausbildung von Aluminiden als intermetallische Phasen handelt es sich bevorzugt um Titan und Zirkon, welche zu Al3Ti bzw. Al3Zr auskristallisieren. Im Falle des Zusatzes von Titan ist die Wiederaufschmelztemperatur im zweiten Schritt des erfindungsgemäßen Verfahrens etwa 800° Celsius. Bei dieser Temperatur ist die Aluminium-Matrix bereits wieder flüssig, das gebildete Titanaluminid, Al3Ti, mit einem Schmelzpunkt von 1460° Celsius ist jedoch noch fest. Aufgrund der geringen Löslichkeit des Al3Ti in der Aluminium-Schmelze von etwa 0,4 % bleiben die Ausscheidungskristalle auch weitestgehend erhalten und werden nicht gelöst. Die Temperatur, auf die das Vormaterial im zweiten Schritt des erfindungsgemäßen Verfahrens wieder aufgewärmt wird, muß deutlich unter der Schmelztemperatur der betreffenden intermetallischen Phase gehalten werden, sie muß jedoch andererseits so hoch sein, dass ein ausreichender Schmelzenanteil für die sich anschließende Umformung in die gewünschten Abmessungen vorhanden ist. Das hieran anschließende Formen oder Umformen kann durch einfaches Schwerkraft-Gießen aber auch im Druck- oder Schleuderkraftguß erfolgen. Die so hergestellten Halbzeuge mit größeren Abmessungen eignen sich vorzüglich für die Umformung z.B. im Strangpressverfahren, Schmieden, Walzen oder Tixocasting, da die feinkörnigen harten Ausscheidungskristalle bei den Umformvorgängen nicht zerstört werden und eine gleichmäßige Verteilung der verschleißmindernden Phasen erreicht wird.When selecting the additive or additives forming the intermetallic phases, it proves to be advantageous to choose those alloy elements which form intermetallic phases, whose melting temperature is as high as possible and whose solubility in the remelted aluminum melt is as low as possible. The intermetallic phases are preferably aluminides, but in principle it could also be compounds of the alloying elements. The alloying elements for forming aluminides as intermetallic phases are preferably titanium and zircon which crystallize out to form Al 3 Ti and Al 3 Zr. If titanium is added, the remelting temperature in the second step of the method according to the invention is about 800 ° Celsius. At this temperature, the aluminum matrix is already liquid again, but the titanium aluminide, Al 3 Ti, with a melting point of 1460 ° Celsius is still solid. Due to the low solubility of the Al 3 Ti in the aluminum melt of about 0.4%, the precipitation crystals are largely preserved and are not dissolved. The temperature to which the starting material is reheated in the second step of the process according to the invention must be kept well below the melting temperature of the intermetallic phase in question, but on the other hand it must be so high that a sufficient proportion of melt for the subsequent shaping into the desired dimensions is available. The subsequent shaping or reshaping can be done by simple gravity casting but also in pressure or centrifugal casting. The semi-finished products with larger dimensions produced in this way are particularly suitable for forming, for example, in the extrusion process, forging, rolling or tixocasting, since the fine-grained, hard precipitation crystals are not destroyed during the forming processes and the wear-reducing phases are evenly distributed.
Zusätzlich zu dem oder den intermetallische Phasen bildenden Zusätzen können solche Zusätze, wie Kupfer, Magnesium, Mangan verwendet werden, welche die Matrixhärte der Legierung erhöhen. Es kann sich darüberhinaus als vorteilhaft erweisen, wenn weitere harte Kristalle, wie z.B. Silizium, in die Aluminium-Matrix eingelagert werden.In addition to the one or more intermetallic phases Additives such as copper, magnesium, manganese can be added be used, which is the matrix hardness of the alloy increase. It can also prove advantageous if other hard crystals, e.g. Silicon into which Aluminum matrix can be stored.
Weitere Merkmale, Einzelheiten und Vorteile der Erfindung ergeben sich aus den beigefügten Ansprüchen. In der Zeichnung zeigt:
Figur 1- ein Schliffbild eines unter Anwendung des erfindungsgemäßen Verfahrens hergestellten Werkstücks und
Figur 2- ein der
Figur 1 entsprechendes Schliffbild eines in einem einzigen Schritt gegossenen Werkstücks.
- Figure 1
- a micrograph of a workpiece produced using the method according to the invention and
- Figure 2
- a micrograph corresponding to FIG. 1 of a workpiece cast in a single step.
Während im Schliffbild nach Figur 2 größere Aussscheidungskristalle einer Abmessung von 100 µm und mehr zu erkennen sind zeigt das Schliffbild nach Figur 1 ein feinkörniges, homogenes Gefüge einer verschleißarmen Aluminium-Legierung, wobei einer Aluminium-Basislegierung Titan und andere die Matrixhärte erhöhende Zusätze zugegeben wurde. Die dunklen Phasen stellen Ausscheidungskristalle dar. Ausgehend von einer Schmelze von ca. 1500 ° Celsius wurde ein Strang in der Größenordnung von ca. 20 mm Durchmesser gegossen und dabei derart schnell zum Erstarren gebracht, dass Ausscheidungskristalle in der Form von Titanaluminid, Al3Ti, homogen verteilt mit einer Abmessung von weniger als 80 µm gebildet werden. Die gewünschte Korngröße wird über die Strangabmessungen und die Wärmeabfuhrbedingungen eingestellt. Der etwa "fingerdicke" Strangguß wird dann in einem zweiten Verfahrensschritt erneut auf eine Temperatur von etwa 800° Celsius gebracht, bei der die Aluminium-Matrix des Vormaterials wenigstens teilweise erschmolzen wird, so dass ein ausreichender Schmelzenanteil für das Formen oder Gießen eines Werkstücks mit gegenüber der Abmessung des fingerdicken Strangs des Vormaterials größerer Abmessung oder für das Gießen eines Halbzeugs, etwa eines dicken Rugels für einen nachfolgenden Strangpressprozess, vorhanden ist. Da die Wiederaufschmelztemperatur im zweiten Schritt des Verfahrens deutlich unterhalb der Schmelztemperatur des Titanaluminids liegt und ferner die Löslichkeit des Titanaluminids in der Aluminium-Schmelze bei der Wiederaufschmelztemperatur lediglich 0,4 % beträgt, bleiben die feinkörnigen Ausscheidungen des Titanaluminids weitestgehend erhalten und kennzeichnen auch das Gefüge des schlußendlichen Werkstücks oder Halbzeugs.While larger precipitation crystals with a dimension of 100 μm and more can be seen in the micrograph according to FIG. 2, the micrograph according to FIG. 1 shows a fine-grained, homogeneous structure of a low-wear aluminum alloy, titanium and other additives increasing the matrix hardness being added. The dark phases represent precipitation crystals. Starting from a melt of approx. 1500 ° Celsius, a strand in the order of magnitude of approx. 20 mm diameter was cast and thereby solidified so quickly that precipitation crystals in the form of titanium aluminide, Al 3 Ti, homogeneously distributed with a dimension of less than 80 microns. The desired grain size is set via the strand dimensions and the heat dissipation conditions. The approximately "finger-thick" continuous casting is then brought back to a temperature of approximately 800 ° Celsius in a second process step, at which the aluminum matrix of the primary material is at least partially melted, so that a sufficient amount of melt for molding or casting a workpiece is compared the dimension of the finger-thick strand of the primary material of larger dimensions or for casting a semi-finished product, such as a thick rug, for a subsequent extrusion process. Since the remelting temperature in the second step of the process is clearly below the melting temperature of the titanium aluminide and, furthermore, the solubility of the titanium aluminide in the aluminum melt at the remelting temperature is only 0.4%, the fine-grained precipitates of the titanium aluminide are largely retained and also characterize the structure of the final workpiece or semi-finished product.
Claims (15)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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DE19649015 | 1996-11-27 | ||
DE19649015A DE19649015A1 (en) | 1996-11-27 | 1996-11-27 | Process for the production of aluminum semi-finished products |
Publications (2)
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EP0845542A1 true EP0845542A1 (en) | 1998-06-03 |
EP0845542B1 EP0845542B1 (en) | 2002-09-25 |
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EP97110712A Expired - Lifetime EP0845542B1 (en) | 1996-11-27 | 1997-07-01 | Process of manufacturing semi-finished products in aluminium |
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DE (2) | DE19649015A1 (en) |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4711823A (en) * | 1984-11-12 | 1987-12-08 | Honda Giken Kogyo Kabushiki Kaisha | High strength structural member made of Al-alloy |
JPH05148563A (en) * | 1991-07-30 | 1993-06-15 | Nippon Steel Corp | Production of electrolytic capacitor electrode material |
JPH07258770A (en) * | 1994-03-18 | 1995-10-09 | Suzuki Motor Corp | Aluminum alloy and its production |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5669346A (en) * | 1979-11-07 | 1981-06-10 | Showa Alum Ind Kk | Aluminum alloy for working and its manufacture |
IT1229029B (en) * | 1989-04-14 | 1991-07-12 | Polvara Maria Crosti Giovanni | PROCESS FOR THE PRODUCTION OF CAST ALUMINUM ALLOYS IN THE SEMI-LIQUID STATE, AS WELL AS PLANT FOR ITS IMPLEMENTATION. |
GB2243620B (en) * | 1990-03-27 | 1994-06-29 | Atsugi Unisia Corp | Improvements in and relating to forming aluminium-silicon alloy |
DE4321640C2 (en) * | 1993-06-30 | 1998-08-06 | Siemens Ag | Process for the directional solidification of a molten metal and casting device for carrying it out |
JPH07109536A (en) * | 1993-10-12 | 1995-04-25 | Nippon Light Metal Co Ltd | Aluminum alloy for forging and heat treatment therefor |
-
1996
- 1996-11-27 DE DE19649015A patent/DE19649015A1/en not_active Withdrawn
-
1997
- 1997-07-01 DE DE59708317T patent/DE59708317D1/en not_active Expired - Lifetime
- 1997-07-01 EP EP97110712A patent/EP0845542B1/en not_active Expired - Lifetime
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4711823A (en) * | 1984-11-12 | 1987-12-08 | Honda Giken Kogyo Kabushiki Kaisha | High strength structural member made of Al-alloy |
JPH05148563A (en) * | 1991-07-30 | 1993-06-15 | Nippon Steel Corp | Production of electrolytic capacitor electrode material |
JPH07258770A (en) * | 1994-03-18 | 1995-10-09 | Suzuki Motor Corp | Aluminum alloy and its production |
Non-Patent Citations (2)
Title |
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DATABASE WPI Section Ch Week 9328, Derwent World Patents Index; Class L03, AN 93-224527, XP002057693 * |
DATABASE WPI Section Ch Week 9549, Derwent World Patents Index; Class M22, AN 95-380414, XP002057694 * |
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Publication number | Publication date |
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DE59708317D1 (en) | 2002-10-31 |
DE19649015A1 (en) | 1998-05-28 |
EP0845542B1 (en) | 2002-09-25 |
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