EP0356718B1 - Procédé pour former par extrusion et modification des propriétés mécaniques des produits semi finis en alliages à partir de poudres métalliques qui ont une résistance augmentée à la chaleur - Google Patents

Procédé pour former par extrusion et modification des propriétés mécaniques des produits semi finis en alliages à partir de poudres métalliques qui ont une résistance augmentée à la chaleur Download PDF

Info

Publication number
EP0356718B1
EP0356718B1 EP89113968A EP89113968A EP0356718B1 EP 0356718 B1 EP0356718 B1 EP 0356718B1 EP 89113968 A EP89113968 A EP 89113968A EP 89113968 A EP89113968 A EP 89113968A EP 0356718 B1 EP0356718 B1 EP 0356718B1
Authority
EP
European Patent Office
Prior art keywords
deformation
cross
extrusion
temperature
alloy
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.)
Expired - Lifetime
Application number
EP89113968A
Other languages
German (de)
English (en)
Other versions
EP0356718A2 (fr
EP0356718A3 (en
Inventor
Malcolm Dr. Couper
Reinhard Fried
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ABB Asea Brown Boveri Ltd
ABB AB
Original Assignee
ABB Asea Brown Boveri Ltd
Asea Brown Boveri AB
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by ABB Asea Brown Boveri Ltd, Asea Brown Boveri AB filed Critical ABB Asea Brown Boveri Ltd
Publication of EP0356718A2 publication Critical patent/EP0356718A2/fr
Publication of EP0356718A3 publication Critical patent/EP0356718A3/de
Application granted granted Critical
Publication of EP0356718B1 publication Critical patent/EP0356718B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/001—Extruding metal; Impact extrusion to improve the material properties, e.g. lateral extrusion
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/01—Extruding metal; Impact extrusion starting from material of particular form or shape, e.g. mechanically pre-treated
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B22F3/04—Compacting only by applying fluid pressure, e.g. by cold isostatic pressing [CIP]
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/002—Making metallic powder or suspensions thereof amorphous or microcrystalline
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • 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

Definitions

  • the invention is based on a method according to the common preamble of the two independent claims 1 and 5.
  • the invention relates to a prior art of molding processes, as is known, for example, from US Pat. No. 4,150,196, in particular column 3, lines 13 to 17.
  • a raw body made of steel powder which is enclosed in a thin metal capsule and compressed by isostatic pressing, is deformed by single or multi-stage hot extrusion to a workpiece which has improved mechanical properties compared to the raw body.
  • the mechanical properties of the workpiece produced in this way are not sufficient for certain applications.
  • the powder In the production of components from alloys produced by powder metallurgy, the powder is generally cold pre-compressed or poured loosely into a metal capsule and then this blank is further compressed in some way by applying pressure and is subjected to a shaping process at the same time or afterwards. Extrusion, especially hot extrusion, plays an important role in the entire production process. The workpiece is then converted into its final shape by pressing, forging, mechanical processing, etc.
  • a peculiarity of extrusion is that the semi-finished product obtained has anisotropic properties. It shows different mechanical properties in different directions, which often makes workpieces made of it unusable.
  • the methods according to the invention are characterized in that they are particularly suitable for the mass production of components for thermal machines.
  • Components manufactured by the method according to the invention have isotropic properties and come very close in shape to the end product.
  • 1 schematically shows the sequence of a first variant of the method with a double cross-sectional tapering of the workpiece.
  • 1 is a first recipient of an extrusion press, in which there is a blank (press body) 2 heated to the temperature T 1, produced by powder metallurgy. 3 is the pressing force prevailing in this first recipient 1.
  • 4 is a second recipient of an extrusion press, 5 the already extruded workpiece located at the temperature T2. 6 is the pressing force. 7 represents the finished semi-finished product. There is a condition that T2 ⁇ T1.
  • FIG. 2 relates to the schematic sequence of a second variant of the method with a cross-sectional taper and a cross-sectional expansion of the workpiece.
  • the left side of FIG. 2 with recipient 1, blank 2 and pressing force 3 corresponds exactly to the left side of FIG. 1.
  • 4 is the second recipient of an extrusion press for expanding the cross-section of the workpiece (pressing body) 5.
  • the extrusion takes place under the pressing force 6 at the temperature T2, which can be equal to or less than T1.
  • 8 is an expanded counterpress cylinder in which a pressing force 9 is exerted in the opposite direction on the finished semi-finished product 7.
  • the finished semi-finished product 7 has the temperature T3, which can be equal to or lower or higher than T1.
  • T2 ⁇ T1
  • T3 can be at least within the framework of the material conditions and can also assume the value of T1.
  • FIG. 5 shows a schematic longitudinal section through an extrusion press for carrying out a second variant of the method in the position immediately after the start of the press.
  • the extrusion press is drawn with the vertical main axis. However, this can take any position in the room and, for example, also lie horizontally.
  • 12 is a fixed table (base plate) of the press
  • 13 is a movable, hydraulically controlled table of the press.
  • 14 is the recipient I (press cylinder) into which the blank, the pressed material 23 to be deformed, is inserted.
  • 15 is the stamp I, which fits into the recipient I.
  • 16 is a press die made of a heat-resistant material.
  • the recipient II counter-press cylinder
  • the punch II counter-punch
  • 19 is an intermediate piece between the table 13 and the recipient 17, which is used for power transmission.
  • 20 is a hydraulically controlled impression cylinder, in which the counter-pressure piston 21 moves. This carries the stamp 18 via a holder 22. In the present case, the diameters of stamp I (15) and counter-stamp II (18) are the same.
  • FIG. 6 shows a schematic longitudinal section through an extrusion press for carrying out a second variant of the method in the position in the second half of the pressing process. All of the reference numerals correspond to those of FIG. 5.
  • FIG. 7 shows a schematic longitudinal section through an extrusion press for carrying out this second variant of the method in the position at the end of the pressing process.
  • the pressing path is exhausted, the recipient I (14) rests with its end face on the table 12.
  • the entire material to be pressed 23 is located in the cavity, which is delimited by the interior of the die 16 and the recipient II (17).
  • the reference symbols correspond exactly to those in FIG. 5.
  • the blank 2 was used as a pressed body in the first recipient 1 of an extrusion press and pressed at a temperature T 1 of 400 ° C and a reduction ratio of 8: 1 to a cylindrical rod of 70 mm in diameter.
  • the creep test showed a service life up to the break of more than 1000 h under a tensile stress of 280 MPa at a temperature of 200 ° C.
  • Example 2 Analogously to Example 1, an alloy was melted, a powder was produced, compressed, degassed and extruded in two steps.
  • the blank 2 had a diameter of 160 mm.
  • the reduction ratio in the 1st step was 5: 1, the temperature T1 430 ° C, the rod diameter 70 mm.
  • the strength values at room temperature were as follows: along across Stretch limit: 440 430 MPa
  • Tensile strenght: 530 520 MPa Elongation (l 5d): 6 1 %
  • Constriction 10th 1 %
  • a piece was cut from the extruded workpiece 5 of 70 mm in diameter and compressed in the extrusion direction at a temperature of 350 ° C. under a forging press in such a way that it assumed a diameter of 100 mm.
  • the workpiece 5 was then inserted into a second recipient 4 of an extrusion press and at a temperature of 280 ° C. with a reduction ratio of 5. 1 pressed into a 45 mm diameter rod.
  • the workpiece was then annealed at 400 ° C for 2 hours. No change in the mechanical properties, in particular no drop in strength, was found.
  • the tensile test at 300 ° C gave a yield strength of 270 MPa, which remained unchanged even after annealing at 300 ° C for 100 h.
  • Example 1 a magnesium alloy was melted and a powder was produced from it.
  • the powder was mechanically alloyed with 0.8% Al2O3 in the attritor for 10 h and in this way an oxide dispersion hardened alloy was produced.
  • the blank 2 of 150 mm in diameter was used in the first recipient of an extrusion press and pressed at a temperature T 1 of 450 ° C and a reduction ratio of 6: 1 to a rod of 60 mm in diameter.
  • Example 3 Similar to Example 3, an oxide dispersion hardened copper alloy was produced.
  • the processing of the powder mixture was carried out exactly as in Example 3.
  • the extrusion reduction ratios and dimensions of the workpiece were the same.
  • the temperature T1 was 800 ° C, the temperature T2 650 ° C.
  • a blank 2 of 75 mm in diameter was used in the first recipient 1 of an extrusion press and pressed at a temperature T 1 of 1050 ° C. and a reduction ratio of 6: 1 to a rod of 30 mm in diameter.
  • a test rod showed very moderate ductility values after recrystallization annealing at 1160 ° C, especially in the transverse direction. The elongation was about 5% longitudinally and less than 1% transversely.
  • Example 2 An aluminum alloy was melted exactly as in Example 1 and atomized to a very fine powder.
  • the powder was first cold isostatically pressed into a green body under a pressure of 4000 bar, welded into an aluminum capsule, degassed under vacuum and hot pressed.
  • the density was 77% of the theoretical value.
  • the blank 2 had a diameter of 30 mm. It was used in the first recipient 1 of an extrusion press and pressed at a temperature T1 of 380 ° C with a reduction ratio of 4: 1 to a rod of 15 mm in diameter.
  • the mechanical properties of the workpiece after this first process step were as follows at room temperature: along across Stretch limit: 380 350 MPa
  • Elongation (l 5d): 4th 2nd %
  • a section of the rod (workpiece 5) of 15 mm in diameter was placed in a second recipient 4 of an extrusion press at a temperature T2 of 450 ° C. with an expansion ratio of 1: 5.5 under a hydrostatic pressure of 4000 bar into the counterpress cylinder 8 ( Press force 9) pressed.
  • the finished semi-finished product 7 had a diameter of 35 mm.
  • the creep test showed a service life up to the break of more than 2000 h under a tensile stress of 260 MPa at a temperature of 210 ° C.
  • the powder was cold-isostatically pressed under a pressure of 4500 bar, sealed in a capsule made of pure magnesium and degassed under vacuum.
  • the blank 2 had a diameter of 60 mm.
  • the blank 2 was used as a compact in the first recipient 1 of an extrusion press and pressed at a temperature T1 of 380 ° C with a reduction ratio of 4: 1 to a cylindrical rod of 30 mm in diameter.
  • a piece of this rod (workpiece 5) was cut off and further processed in an extruder in a second recipient 4.
  • the extrusion press had a cross-sectional constriction (Die) 10 and an extended counterpressure cylinder 8.
  • Die cross-sectional constriction
  • T3 a temperature T3 of 250 ° C.
  • the reduction ratio was 3: 1, so that the workpiece 11 in the constriction 10 still had a diameter of 17 mm.
  • the expansion ratio was 1: 3.
  • the finished semi-finished product 7 thus had a diameter of 30 mm.
  • the blank 2 was then further processed in an extrusion press with a first recipient 1 and an expanded counter-press cylinder 8 and a cross-sectional constriction 10.
  • the temperature T1 was 700 ° C, the temperature T3 650 ° C.
  • the reduction ratio was 4.5: 1, so that the strand still had a diameter of 14 mm.
  • the expansion ratio was 1: 5.
  • the finished semi-finished product 7 had a diameter of 32 mm.
  • the mechanical strength values at room temperature were: along across Stretch limit: 580 535 MPa
  • Elongation (l 5d): 4.5 4th %
  • Constriction 10th 9 %
  • An oxide dispersion-hardened nickel-based superalloy with the trade name MA 6000 was chosen as the alloy: the composition can be seen from Example 5.
  • the starting material corresponded exactly to the information given under this example.
  • a blank of 40 mm in diameter was inserted into the recipient I (14 in FIG. 5) of a double-acting extrusion press and pressed through the press die 16 by means of a punch I (15) with a reduction ratio of 4: 1.
  • the temperature in recipient I was 980 ° C.
  • a reciprocal pressure of 10,000 bar was built up in recipient II (17) as a hydrostatically acting pressure by means of stamp II (18).
  • Both recipients (14, 17) were reinforced with cooled, external reinforcement rings in order to withstand the respectable pressures.
  • the press die 16 consisted of the molybdenum alloy TZM, was reinforced by outer rings and had a bore of 15 mm in diameter.
  • the recipient II had a bore of 30 mm in diameter, so that the expansion ratio was 1: 4.
  • the temperature T3 in recipient II was 1030 ° C.
  • the mechanical values at room temperature were as follows (after zone annealing): along across Stretch limit: 960 540 MPa
  • Elongation (l 5d): 6 3.5 %
  • the invention is not restricted to the exemplary embodiments.
  • the method is carried out by successively performing the deformation in at least two different temperature ranges, the material being first reduced in its cross section in an upper temperature range T 1 by hot extrusion and then deformed again in a lower temperature range T 2 by hot extrusion , with its cross-section being further reduced.
  • the alloy with increased heat resistance is a precipitation hardenable high temperature aluminum alloy made from oversaturated melt by extremely high cooling rate or an oxide dispersion hardened magnesium alloy or a precipitation hardenable oxide dispersion hardened copper alloy or an oxide dispersion hardened nickel base superalloy.
  • the first deformation in the temperature range T1 from 360 to 450 ° C with a first reduction ratio of 4: 1 to 8: 1 and the second deformation in the temperature range T2 from 200 to 350 ° C with a second reduction ratio of 2 : 1 to 6: 1 carried out such that the total reduction ratio is 8: 1 to 40: 1.
  • the blank 2 made of powder-metallurgically produced aluminum alloy is cold-isostatically pre-pressed and degassed or cold-isostatically pre-pressed, degassed and further cold or hot compressed.
  • the workpiece is deformed between the two extrusion process steps by upsetting in the extrusion direction (hot forging) in such a way that its cross section is expanded.
  • the method is also carried out by performing the deformation in at least two phases, the material being first reduced in its cross section in a first temperature range T 1 by hot extrusion and then in a second temperature range T 2; T3 is deformed again by hot extrusion, its cross section being expanded again in such a way that it is immediately behind the die 10; 16 is forced to a relatively sharp-edged deflection and to flow transversely to the extrusion direction.
  • the first deformation in the temperature range T1 from 360 to 450 ° C with a reduction ratio of 4: 1 and the second, the expansion of the cross section serving deformation in the temperature range T2; T3 from 200 to 500 ° C with an expansion ratio of 1: 2 to 1: 8 performed.
  • the second deformation which serves to expand the cross-section, can just cancel itself out, so that the product becomes 1 and, in the end, the workpiece has the unchanged cross section of the blank.
  • the existing cross-section reduction and cross-section expansion is a cross-section reduction by extrusion with a reduction ratio of 4: 1 to 8: 1 in the temperature range T1 of 360 to 450 ° C upstream.
  • the second deformation is advantageously carried out under hydrostatic pressure or under superimposition of isostatic pressure in the sense of a combined extrusion and hot isostatic pressing.
  • the first and second deformations are preferably carried out simultaneously, but locally separated, in an extrusion press which consists of two recipients 14; 19, an intermediate die 16 and two punches 15; 18, the latter executing an axial movement in the same direction with respect to the center of the die 16.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Fluid Mechanics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)

Claims (14)

  1. Procédé de façonnage d'ébauches (2) produites par la métallurgie des poudres en un alliage à résistance à la chaleur accrue, dans lequel les ébauches (2) sont déformées par filage à la presse à chaud en plusieurs stades en des objets à travailler possédant des propriétés mécaniques améliorées, caractérisé en ce qu'à titre d'alliage à résistance à la chaleur accrue, on utilise un alliage d'aluminium à haute température pouvant être trempé par précipitation et élaboré à partir d'une masse fondue sursaturée par une vitesse de refroidissement extrêmement élevée, un alliage d'aluminium durci par dispersion d'oxyde, un alliage de cuivre durci par dispersion d'oxyde et pouvant être trempé par précipitation ou un superalliage à base de nickel durci par dispersion d'oxyde, que, pendant l'exécution du filage à la presse à chaud en plusieurs stades, lors d'une première déformation, les ébauches (2) sont réduites en section transversale dans un premier domaine de températures (T₁) avec formation de précurseurs d'objets à travailler et que, lors d'une seconde déformation suivante pendant le filage à la presse à chaud, les précurseurs sont réduits en section transversale dans un second domaine de températures (T₂) qui est inférieur au premier domaine de températures (T₁), avec formation des objets à travailler.
  2. Procédé suivant la revendication 1, caractérisé en ce que l'alliage est un alliage d'aluminium à haute température et que la première déformation est effectuée entre 360°C et 450°C avec un premier rapport de réduction de 4 : 1 à 8 : 1 et la seconde déformation est effectuée entre 200°C et 350°C avec un second rapport de réduction de 2 : 1 à 6 : 1, de telle façon que le rapport de réduction total soit 8 : 1 à 40 : 1.
  3. Procédé suivant la revendication 2, caractérisé en ce que les ébauches (2) sont précomprimées à froid et de manière isostatique et dégazées ou précomprimées à froid et de manière isostatique, dégazées et ensuite comprimées à froid ou à chaud.
  4. Procédé suivant l'une quelconque des revendications 1 à 3, caractérisé en ce que les précurseurs des objets produits par la première déformation sont forgés à chaud avant la seconde déformation par refoulement dans la direction de filage à la presse, de telle façon que leur section transversale soit augmentée.
  5. Procédé de façonnage d'ébauches (2) produites par la métallurgie des poudres en un alliage à résistance à la chaleur accrue, dans lequel les ébauches (2) sont déformées par filage à la presse à chaud, en plusieurs stades, en des objets à travailler possédant des propriétés mécaniques améliorées, caractérisé en ce que, pendant l'exécution du filage à la presse à chaud, en plusieurs stades, lors d'une première déformation, les ébauches (2) sont réduites en section transversale dans un premier domaine de températures (T₁) avec formation de précurseurs des objets à travailler, et que, lors d'une seconde déformation qui suit le filage à la presse à chaud, les précurseurs sont agrandis en section transversale dans un second domaine de températures (T₂, T₃) avec formation des objets à travailler, de telle sorte que les sections transversales immédiatement derrière une filière (10; 16) utilisée pour le filage à la presse à chaud, subissent une déviation à angle relativement vif et un fluage transversal à la direction de filage à la presse.
  6. Procédé suivant la revendication 5, caractérisé en ce qu'à titre d'alliage à résistance à la chaleur accrue, on utilise un alliage d'aluminium à haute température pouvant être trempé par précipitation, élaboré à partir d'une masse fondue sursaturée par une vitesse de refroidissement extrêmement élevée, un alliage de magnésium durci par dispersion d'oxyde, un alliage de cuivre durci par dispersion d'oxyde et pouvant être trempé par précipitation ou un superalliage à base de nickel durci par dispersion d'oxyde.
  7. Procédé suivant la revendication 6, caractérisé en ce que l'alliage est un alliage d'aluminium à haute température et que la première déformation est effectuée dans le domaine de températures (T₁) de 360 à 450°C avec un rapport de réduction de 4 : 1 et la seconde déformation, servant à augmenter la section transversale, est effectuée dans le domaine de températures (T₂; T₃) de 200 à 500°C avec un rapport d'agrandissement de 1 : 2 à 1 : 8.
  8. Procédé suivant la revendication 7, caractérisé en ce que la seconde déformation servant à augmenter la section transversale est effectuée à une température (T₂; T₃) qui est inférieure à la température (T₁) de la première déformation.
  9. Procédé suivant la revendication 7, caractérisé en ce que la seconde déformation servant à augmenter la section transversale est effectuée à une température (T₂; T₃) qui est supérieure à la température (T₁) de la première déformation.
  10. Procédé suivant la revendication 7, caractérisé en ce que la réduction de section transversale de la première déformation et l'augmentation de section transversale de la seconde déformation s'annulent mutuellement, de sorte que le produit devient égal à 1 et qu'en fin de compte, la pièce présente la section transversale non modifiée de l'ébauche.
  11. Procédé suivant la revendication 10, caractérisé en ce que la déformation constituée d'une réduction de section transversale et d'une augmentation de section transversale est précédée d'une réduction de section transversale par filage à la presse avec un rapport de réduction de 4 : 1 à 8 : 1 dans le domaine de températures (T₁) de 360 à 450°C.
  12. Procédé suivant la revendication 5, caractérisé en ce que la seconde déformation est effectuée sous pression hydrostatique ou superposition d'une pression isostatique dans le sens d'un pressage par filage à la presse et combiné avec un pressage par compression isostatique à chaud.
  13. Procédé suivant la revendication 5, caractérisé en ce que la première et la seconde déformation sont effectuées simultanément, mais en des endroits séparés dans une presse à filer qui est constituée de deux conteneurs (14; 19), d'une filière de presse intermédiaire (16) et de deux poinçons (15; 18), ces derniers effectuant des mouvements axiaux dans le même sens par rapport au centre de la filière de presse (16).
  14. Procédé suivant l'une quelconque des revendications 5 à 13, caractérisé en ce que l'ébauche (2) en alliage d'aluminium élaboré par la métallurgie des poudres est précomprimée à froid et de manière isostatique et dégazée ou est précomprimée à froid et de manière isostatique, dégazée et à nouveau comprimée à froid ou à chaud.
EP89113968A 1988-08-02 1989-07-28 Procédé pour former par extrusion et modification des propriétés mécaniques des produits semi finis en alliages à partir de poudres métalliques qui ont une résistance augmentée à la chaleur Expired - Lifetime EP0356718B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CH2895/88 1988-08-02
CH289588 1988-08-02

Publications (3)

Publication Number Publication Date
EP0356718A2 EP0356718A2 (fr) 1990-03-07
EP0356718A3 EP0356718A3 (en) 1990-03-21
EP0356718B1 true EP0356718B1 (fr) 1994-01-19

Family

ID=4244013

Family Applications (1)

Application Number Title Priority Date Filing Date
EP89113968A Expired - Lifetime EP0356718B1 (fr) 1988-08-02 1989-07-28 Procédé pour former par extrusion et modification des propriétés mécaniques des produits semi finis en alliages à partir de poudres métalliques qui ont une résistance augmentée à la chaleur

Country Status (4)

Country Link
US (1) US4992238A (fr)
EP (1) EP0356718B1 (fr)
JP (1) JPH02163305A (fr)
DE (2) DE3919107A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006043502A1 (de) * 2006-09-12 2008-03-27 Technische Universität Berlin Verfahren und Vorrichtung zum Herstellen eines gepreßten Stranges mittels Strangpressen

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04272616A (ja) * 1991-02-27 1992-09-29 Aisin Seiki Co Ltd 超電導線材及びその製造方法
US5561829A (en) * 1993-07-22 1996-10-01 Aluminum Company Of America Method of producing structural metal matrix composite products from a blend of powders
DE19747257C2 (de) * 1997-10-25 2001-04-26 Geesthacht Gkss Forschung Vorrichtung zur Kapselung von Rohlingen aus metallischen Hochtemperatur-Legierungen
US7625520B2 (en) * 2003-11-18 2009-12-01 Dwa Technologies, Inc. Manufacturing method for high yield rate of metal matrix composite sheet production
ITTO20040169A1 (it) * 2004-03-15 2004-06-15 Teksid Aluminum S R L Sistema di tenuta per recipienti ad alte pressioni ed alte temperature
TWI598161B (zh) * 2016-03-04 2017-09-11 中原大學 金屬射出與反壓系統及其方法
CN114345970B (zh) * 2021-12-06 2023-09-22 江苏理工学院 一种高强耐蚀铝合金钻杆及其制备方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1144595A (en) * 1910-03-25 1915-06-29 Westinghouse Lamp Co Process for manufacturing incandescent filaments.
US3084042A (en) * 1960-02-23 1963-04-02 Du Pont Metal production
US3226267A (en) * 1962-03-26 1965-12-28 Dow Chemical Co High strength aluminum alloy extrusion process and product
US3899325A (en) * 1969-07-14 1975-08-12 Minnesota Mining & Mfg Method of making a closed end tube
US3955933A (en) * 1972-02-29 1976-05-11 The United States Of America As Represented By The Secretary Of The Navy Magnesium-boron particulate composites
US3922182A (en) * 1973-01-22 1975-11-25 Int Nickel Co Alloy adapted for furnace components
US4150196A (en) * 1974-04-19 1979-04-17 Granges Nyby Ab Method of producing tubes or the like and capsule for carrying out the method as well as blanks and tubes according to the method
DE2419014C3 (de) * 1974-04-19 1985-08-01 Nyby Bruks AB, Nybybruk Verfahren zum Herstellen von Rohren aus rostfreiem Stahl und Anwendung des Verfahrens auf das Herstellen von Verbundrohren
US4605599A (en) * 1985-12-06 1986-08-12 Teledyne Industries, Incorporated High density tungsten alloy sheet
CH675089A5 (fr) * 1988-02-08 1990-08-31 Asea Brown Boveri

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006043502A1 (de) * 2006-09-12 2008-03-27 Technische Universität Berlin Verfahren und Vorrichtung zum Herstellen eines gepreßten Stranges mittels Strangpressen
DE102006043502B4 (de) * 2006-09-12 2008-11-27 Technische Universität Berlin Verfahren und Vorrichtung zum Herstellen eines gepreßten Stranges mittels Strangpressen

Also Published As

Publication number Publication date
DE58906745D1 (de) 1994-03-03
EP0356718A2 (fr) 1990-03-07
EP0356718A3 (en) 1990-03-21
DE3919107A1 (de) 1990-02-08
JPH02163305A (ja) 1990-06-22
US4992238A (en) 1991-02-12

Similar Documents

Publication Publication Date Title
EP0464366B1 (fr) Procédé de fabrication d'une pièce en alliage à base d'aluminiure de titane contenant un matériau de dopage
EP0192105B1 (fr) Méthode pour former à chaud au moins une feuille de métal d'une matière difficilement déformable
EP3069802B1 (fr) Procédé de production d'un composant en matériau composite doté d'une matrice en métal et de phases intercalaires inter-métalliques
DE2419014C3 (de) Verfahren zum Herstellen von Rohren aus rostfreiem Stahl und Anwendung des Verfahrens auf das Herstellen von Verbundrohren
EP0035601B1 (fr) Procédé de fabrication d'un alliage-mémoire
EP0965412B1 (fr) Procédé pour la production d'une soupape à champignon à base d'une alliage de TiAl
DE2542094A1 (de) Metallpulver, verfahren zur behandlung losen metallpulvers und verfahren zur herstellung eines verdichteten presslings
DE1783134B2 (de) Verfahren zur pulvermetallurgischen Herstellung von Hartlegierungen. Ausscheidung aus: 1533275 Annu Latrobe Steel Co., Latrobe, Pa. (V.StA.)
DE2303802A1 (de) Verfahren zur waermebehandlung einer dispersionsverfestigten, hitzebestaendigen knetlegierung
DE2362499C2 (de) Verfahren zur pulvermetallurgischen Herstellung von Strangprßkörpern
EP0035602B1 (fr) Procédé de préparation par métallurgie des poudres d'un alliage-mémoire à base de cuivre, de zinc et d'aluminium
AT411027B (de) Vorrichtung und verfahren zur herstellung feinkristalliner werkstoffe
DE1283547B (de) Verfahren zum Erhoehen der Zugfestigkeit, Dehngrenze und Zeitstandfestigkeit und zurStabilisierung der Kornorientierung von dispersionsgehaerteten Legierungen
EP0356718B1 (fr) Procédé pour former par extrusion et modification des propriétés mécaniques des produits semi finis en alliages à partir de poudres métalliques qui ont une résistance augmentée à la chaleur
EP0328898A1 (fr) Procédé pour la fabrication d'une pièce résistant à la chaleur d'une ébauche réalisée par métallurgie des poudres à ductibilité transversale élevée en alliage d'aluminium
EP0396185B1 (fr) Procédé pour la préparation d'outils semi-finis résistant au fluage en métal réfractaire
AT5199U1 (de) Formteil aus einem intermetallischen gamma-ti-al-werkstoff
DE2443187C2 (de) Verfahren zum Herstellen von Flachwalzprodukten aus mechanisch legierten Pulvern
EP0545145B1 (fr) Fabrication de pièces poreuses à base de cuivre comme un produit semi-fini pour un traitement d'usinage
DE3113733C2 (de) Verfahren zur Rückgewinnung von hochwertigen Werkstoffen
EP0035070B1 (fr) Alliage-mémoire à base d'une solution solide riche en cuivre ou en nickel
EP0045984B1 (fr) Procédé pour la fabrication de pièces en un alliage résistant aux températures élevées
DE1920466A1 (de) Verfahren zum Verfestigen von Werkstuecken
EP0074679B1 (fr) Procédé pour la fabrication d'ébauches en un alliage résistant à la chaleur
DE2108978A1 (de) Verfahren zur Herstellung von Superlegierungen

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

PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A2

Designated state(s): CH DE FR GB LI SE

AK Designated contracting states

Kind code of ref document: A3

Designated state(s): CH DE FR GB LI SE

17P Request for examination filed

Effective date: 19900810

17Q First examination report despatched

Effective date: 19920717

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): CH DE FR GB LI SE

REF Corresponds to:

Ref document number: 58906745

Country of ref document: DE

Date of ref document: 19940303

GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)

Effective date: 19940325

ET Fr: translation filed
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
EAL Se: european patent in force in sweden

Ref document number: 89113968.5

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 19950615

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 19950621

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 19950626

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 19950731

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: CH

Payment date: 19950803

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Effective date: 19960728

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Effective date: 19960729

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Effective date: 19960731

Ref country code: CH

Effective date: 19960731

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 19960728

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Effective date: 19970328

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Effective date: 19970402

EUG Se: european patent has lapsed

Ref document number: 89113968.5

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST