EP0199715A2 - Process for manufacturing steel wire - Google Patents

Process for manufacturing steel wire Download PDF

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Publication number
EP0199715A2
EP0199715A2 EP86890113A EP86890113A EP0199715A2 EP 0199715 A2 EP0199715 A2 EP 0199715A2 EP 86890113 A EP86890113 A EP 86890113A EP 86890113 A EP86890113 A EP 86890113A EP 0199715 A2 EP0199715 A2 EP 0199715A2
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EP
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Prior art keywords
deformation
temperature
wire
treatment temperature
steel wire
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EP86890113A
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German (de)
French (fr)
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EP0199715A3 (en
Inventor
Ernst Dipl.-Ing. Siegmund
Ernst Dipl.-Ing. Hojas
Günter Dipl.-Ing. Hampejs
Helmut Eggenreich
Erwin Kraushofer
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Voestalpine Wire Rod Austria GmbH
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Voestalpine Wire Rod Austria GmbH
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Publication of EP0199715A2 publication Critical patent/EP0199715A2/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires

Definitions

  • the invention relates to a method for producing steel wire with high tensile strength and low creep and relaxation properties, in which the steel wire is subjected to deformation and heat treatment.
  • Steel wires with low reiaxation properties have hitherto been produced by cold working, for example by drawing or rolling. This is followed by heat treatment under tensile stress, depending on the steel grade selected, at temperatures between 200 and 600 ° C and cooling to room temperature.
  • the invention now aims to achieve this. to produce a cold-formed steel wire with high tensile strength and particularly low creep and relaxation properties and to work with this method in addition to ensuring the high strength values with as little energy expenditure as possible.
  • the invention essentially consists in that the steel wire is heated to a temperature lower than the temperature required for the heat treatment, which plus the heat of deformation with a deformation of up to 50% decrease in cross-section, the desired treatment temperature before entering the last deformation step results, and that after this deformation, the steel wire is stretched at the treatment temperature.
  • the cooling then takes place in a known manner by means of suitable cooling units. It is shown that when the process is carried out in this way, in addition to achieving particularly low creep and relaxation properties and in addition to saving energy, a higher tensile strength of the end product produced can be observed in comparison with conventionally produced products.
  • the tensile forces required for the deformation are used for stretching at the treatment temperature.
  • the temperature increase resulting from the heat of deformation in the last deformation stage depends on the degree of deformation of this last stage and on the diameter of the drawn wire. Taking these parameters into account, it has proven to be particularly advantageous within the scope of the method according to the invention to carry out the heat treatment at temperatures between 200 ° C. and the recrystallization temperature of the steel, in particular between 250 ° C. and 600 ° C., and the heating before the last deformation step in the If drawing dies are used at temperatures from 30 to 100 ° C. below the desired treatment temperature and in the case of using rollers before the last roll pass to temperatures of 30 to 80 ° G below the desired treatment temperature.
  • the method according to the invention is particularly suitable for the production of steel wires, in particular prestressed concrete wires, and can advantageously also be used for spring steel wires and high-strength steel cable wires.
  • a major advantage of the process control according to the invention is that the wire does not have to be heated to the full treatment temperature and a small amount of force is additionally required for drawing. This results in a large saving in energy expenditure. When using this method, good results were achieved in a particularly simple manner in relation to the low relaxation of the steel wires and an extraordinarily large increase in tensile strength in the last deformation step.
  • the deformation is preferably carried out with a 10 to 40% decrease in cross-section, the corresponding temperature being added to the treatment temperature.
  • the method according to the invention is advantageously suitable for unalloyed steel grades with 0.30 to 1.20% by weight of carbon or alloyed steels with up to 5% by weight of manganese and up to 3% by weight of silicon.
  • FIG. 2 a modified arrangement analogous to FIG. 1 using a roll stand.
  • 1 denotes the steel wire to be processed, preferably already cold-formed, which is subjected to heating at 2 to a temperature which is lower than the temperature required for the treatment.
  • 3 the last deformation stage is designated with one or more drawing dies. 3 follows a cooling device 4, in which the steel wire is cooled in a suitable manner. The cooled wire is fed to a device 5. In this device 5, the tensile force required for the deformation of the wire is brought up. In the distance between 3 and 4, this tensile force causes the wire to stretch at the treatment temperature.
  • the pre-rolled, preferably already cold-formed, wire is designated by 1.
  • the heating unit 2 is arranged before the last deformation stage in the form of a roller pass.
  • the rolling process by non-driven rolls is indicated schematically by the roll stand 6.
  • cooling takes place in an analog cooling device 4, as has already been shown in FIG. A device 5 is then again provided.
  • a preferred wire with a diameter of 8.1 mm was heated to a temperature of 320 ° C. before entering the last drawing die. At this temperature, the diameter was subsequently drawn to 7.0 mm, an increase in temperature from 80 ° C. starting from 320 ° to 400 ° C. being observed.
  • the wire consisted of unalloyed steel with a carbon content of 0.83% by weight and a manganese content of 0.66% by weight. After the treatment according to the invention, a tensile strength of 1850 N / mm 2 was found. Before the treatment, the wire had a tensile strength of 1630 N / mm 2 .
  • the relaxation test of the material treated according to the invention under an initial load of 70% of the breaking load showed a voltage drop of 0.95% after 1000 hours.
  • a treatment according to the prior art was carried out with the same starting material, drawn wire with a diameter of 8.1 mm and a tensile strength of 1630 N / mm 2 .
  • the wire was drawn in the usual way and then subjected to the treatment temperature, after which a tensile strength of 1740 N / mm 2 was established.
  • a pre-drawn wire with a diameter of 14 mm was used. It was an unalloyed steel with a carbon content of 0.78% by weight and a manganese content of 0.75% by weight.
  • the wire was heated to a temperature of 400 ° C. During the rolling process by drag rolling, the temperature rose by a further 45 ° C to 445 ° C. The tensile strength measured after this treatment and cooling was 1690 N / mm 2 .
  • the relaxation test showed a voltage drop of 1.2% after 1000 hours, measured on the initial load of 70% of the breaking load.
  • treatment temperatures between 200 ° C. and the recrystallization temperature of the steel are used in the process according to the invention, deformations of up to 50% reduction in cross section, preferably 10 to 35%, being used.
  • the method according to the invention is primarily suitable for the treatment of unalloyed steel types with 0.30 to 1.20% by weight of carbon or for alloyed steels with up to 5% by weight of manganese and up to 3% by weight of silicon.

Abstract

Steel wire of high tensile strength and low creep properties and relaxation properties is manufactured by heating the material before deformation and stretching it at the treatment temperature after the deformation. In this process, the wire is heated to a lower temperature than the treatment temperature before it enters the last deformation stage. The temperature increase to the required treatment temperature is effected by the deformation energy. In the last deformation stage, deformations of up to a 50 % reduction in cross-section are applied. The tensile force required for the deformation is utilised for the stretching. <IMAGE>

Description

Die Erfindung bezieht sich auf ein Verfahren zur Herstellung von Stahldraht mit hoher Zugfestigkeit und niedrigen Kriech5 und Relaxationseigenschaften, bei welchem der Stahldraht einer Verformung und einer Wärmebehandlung unterzogen wird.The invention relates to a method for producing steel wire with high tensile strength and low creep and relaxation properties, in which the steel wire is subjected to deformation and heat treatment.

Aus der AT-PS 32 609 ist ein Verfahren zur Verhinderung des Hartziehens des Drahtes beim Ziehen von Stahldraht bekanntgeworden, wobei zwischen den einzelnen Verformungsschritten jeweils eine Kühlung des Drahtes vorgenommen wird, um unerwünschte Festigkeitsänderungen zu verhindern. Beim Ziehen wird der Draht erhitzt, wodurch die Härte und Sprödigkeit des Drahtes beseitigt wird, worauf durch Abkühlung nach jeder Verformungsstufe der ursprüngliche Zustand des Drahtes wieder hergestellt werden soll, um eine weiterführende Verformung zu ermöglichen.From AT-PS 32 609 a method for preventing hard drawing of the wire when drawing steel wire has become known, the wire being cooled between the individual deformation steps in order to prevent undesirable changes in strength. When the wire is drawn, it is heated, which eliminates the hardness and brittleness of the wire, after which the wire should be restored to its original state by cooling after each deformation step in order to allow further deformation.

Stahldrähte mit niedrigen Reiaxationseigenschaften wurden bisher durch Kaltverformung, beispielsweise durch Ziehen oder Walzen, hergestellt. Anschließend daran erfolgt eine Wärmebehandlung unter Zugspannung in Abhängigkeit von der gewählten Stahlsorte bei Temperaturen zwischen 200 und 600°C und eine Abkühlung auf Raumtemperatur.Steel wires with low reiaxation properties have hitherto been produced by cold working, for example by drawing or rolling. This is followed by heat treatment under tensile stress, depending on the steel grade selected, at temperatures between 200 and 600 ° C and cooling to room temperature.

Die Erfindung zielt nun darauf. ab, einen kaltverformten Stahldraht mit hoher Zugfestigkeit und besonders niedrigen Kriech-und Relaxationseigenschaften herzustellen und bei diesem Verfahren neben der Sicherstellung der hohen Festigkeitswerte mit möglichst geringem Energieaufwand zu arbeiten.The invention now aims to achieve this. to produce a cold-formed steel wire with high tensile strength and particularly low creep and relaxation properties and to work with this method in addition to ensuring the high strength values with as little energy expenditure as possible.

Zur Lösung dieser Aufgabe besteht die Erfindung im wesentlichen darin, daß der Stahldraht vor Eintritt in die letzte Verformungsstufe auf eine gegenüber der für die Wärmebehandlung erforderlich Temperatur geningere Temperatur erwärmt wird, welche zuzüglich der Verformungswärme bei einer Verformung von bis zu 50 % Querschnittsabnahme die gewünschte Behandlungstemperatur ergibt, und daß nach dieser Verformung der Stahldraht bei der Behandlungstemperatur gereckt wird. Die Abkühlung erfolgt anschließend in bekannter Weise durch geeignete Kühlaggregate. Es zeigt sich, daß bei Führung des Verfahrens auf diese Weise neben der Erzielung besonders niedriger Kriech-und Relaxationseigenschaften und neben einer Einspa-rung an Energie auch eine höhere Zugfestigkeit des erzeugten Endproduktes im Vergleich mit konventionell hergestellten Produkten beobachtet werden kann. Die für die Verformung erforderlichen Zugkräfte werden für eine Reckung bei Behandlungstemperatur ausgenützt.To achieve this object, the invention essentially consists in that the steel wire is heated to a temperature lower than the temperature required for the heat treatment, which plus the heat of deformation with a deformation of up to 50% decrease in cross-section, the desired treatment temperature before entering the last deformation step results, and that after this deformation, the steel wire is stretched at the treatment temperature. The cooling then takes place in a known manner by means of suitable cooling units. It is shown that when the process is carried out in this way, in addition to achieving particularly low creep and relaxation properties and in addition to saving energy, a higher tensile strength of the end product produced can be observed in comparison with conventionally produced products. The tensile forces required for the deformation are used for stretching at the treatment temperature.

Die durch die Verformungswärme in der letzten Verformungsstufe entstehende Temperaturerhöhung ist abhängig vom Verformungsgrad dieser letzten Stufe und vom Durchmesser des vorgezogenen Drahtes. Unter Berücksichtigung dieser Parameter hat es sich im Rahmen des erfindungsgemäßen Verfahrens als besonders vorteilhaft erwiesen, die Wärmebehandlung bei Temperaturen zwischen 200°C und der Rekristallisationstemperatur des Stahles, insbesondere zwischen 250°C und 600°C, vorzunehmen und die Erwärmung vor der letzten Verformungsstufe im Falle der Verwendung von Ziehsteinen auf Temperaturen von 30 bis 100 ° C unterhalb der gewünschten Behandlungstemperatur und im Falle der Verwendung von Walzen vor dem letzten Walzenstich auf Temperaturen von 30 bis 80°G unterhalb der gewünschten Behandlungstemperatur vorzunehmen.The temperature increase resulting from the heat of deformation in the last deformation stage depends on the degree of deformation of this last stage and on the diameter of the drawn wire. Taking these parameters into account, it has proven to be particularly advantageous within the scope of the method according to the invention to carry out the heat treatment at temperatures between 200 ° C. and the recrystallization temperature of the steel, in particular between 250 ° C. and 600 ° C., and the heating before the last deformation step in the If drawing dies are used at temperatures from 30 to 100 ° C. below the desired treatment temperature and in the case of using rollers before the last roll pass to temperatures of 30 to 80 ° G below the desired treatment temperature.

Das erfindungsgemäße Verfahren eignet sich hiebei im besonderen für die Herstellung von Stahldrähten, insbesondere von Spannbetondrähten, und kann in vorteilhafter Weise auch bei Federstahldrähten und hochfesten Stahlseildrähten angewendet werden. Ein wesentlicher Vorteil der erfindungsgemäßen Verfahrensführung liegt hiebei darin, daß der Draht nicht auf die volle Behandlungstemperatur erwärmt werden muß und zusätzlich ein geringer Kraftaufwand für das Ziehen erforderlich ist Dadurch ergibt sich eine große Einsparung im Energieaufwand. Bei Anwendung dieses Verfahrens wurden in besonders einfacher Weise gute Ergebnisse in bezug auf die niedrige Relaxation der Stahldrähte und ein außergewöhnlich großer Zuwachs der Zugfestigkeit in der letzten Verformungsstufe erreicht.The method according to the invention is particularly suitable for the production of steel wires, in particular prestressed concrete wires, and can advantageously also be used for spring steel wires and high-strength steel cable wires. A major advantage of the process control according to the invention is that the wire does not have to be heated to the full treatment temperature and a small amount of force is additionally required for drawing. This results in a large saving in energy expenditure. When using this method, good results were achieved in a particularly simple manner in relation to the low relaxation of the steel wires and an extraordinarily large increase in tensile strength in the last deformation step.

In vorteilhafter Weise wird die Verformung vorzugsweise mit 10 bis 40 % Querschnittsabnahme durchgeführt, wobei die entsprechende Temperaturergänzung auf die Behandlungstemperatur vorgenommen wird. Das erfindungsgemäße Verfahren eignet sich in vorteilhafter Weise für unlegierte Stahlsorten mit 0,30 bis 1,20 Gew.% Kohlenstoff oder legierte Stähle mit bis zu 5 Gew.% Mangan und bis zu 3 Gew.% Silizium.Advantageously, the deformation is preferably carried out with a 10 to 40% decrease in cross-section, the corresponding temperature being added to the treatment temperature. The method according to the invention is advantageously suitable for unalloyed steel grades with 0.30 to 1.20% by weight of carbon or alloyed steels with up to 5% by weight of manganese and up to 3% by weight of silicon.

Die Erfindung wird nachfolgend an Hand von Ausführungsbeispielen und in der Zeichnung - schematisch dargestellten Ausführungsbeispielen von für die Durchführung des erfindungsgemäßen Verfahrens geeigneten Vorrichtungen näher erläutert. In der Zeichnung zeigen Fig.1 eine Anordnung von Einrichtungen für die DurchführungThe invention is explained in more detail below on the basis of exemplary embodiments and schematically illustrated exemplary embodiments of devices suitable for carrying out the method according to the invention in the drawing. 1 shows an arrangement of devices for the implementation

des erfindungsgemäßen Verfahrens unter Verwendung von Ziehsteinen und Fig.2 eine abgewandelte Anordnung analog der Fig.1 unter Verwendung eines Walzgerüstes.of the method according to the invention using drawing dies and FIG. 2 a modified arrangement analogous to FIG. 1 using a roll stand.

In Fig.1 ist mit 1 der zu verarbeitende, vorzugsweise bereits kaltverformte, Stahldraht bezeichnet, welcher bei 2 einer Erwärmung auf eine Temperatur unterworfen wird, welche geringer ist als die für die Behandlung erforderliche Temperatur. Mit 3 ist die letzte Verformungsstufe mit einem oder mehreren Ziehsteinen bezeichnet. Anschließend an 3 folgt eine Abkühlvorrichtung 4, in welcher der Stahldraht in geeigneter Weise abgekühlt wird. Der abgekühlte Draht wird einer Vorrichtung 5 zugeführt. In dieser Vorrichtung 5 wird die für die Verformung des Drahtes erforderliche Zugkraft aufge bracht. In der Strecke zwischen 3 und 4 bewirkt diese Zugkraft eine Reckung des Drahtes bei der Behandlungstemperatur.In FIG. 1, 1 denotes the steel wire to be processed, preferably already cold-formed, which is subjected to heating at 2 to a temperature which is lower than the temperature required for the treatment. With 3 the last deformation stage is designated with one or more drawing dies. 3 follows a cooling device 4, in which the steel wire is cooled in a suitable manner. The cooled wire is fed to a device 5. In this device 5, the tensile force required for the deformation of the wire is brought up. In the distance between 3 and 4, this tensile force causes the wire to stretch at the treatment temperature.

Bei der Darstellung nach Fig.2 ist mit 1 wiederum der vorgewalzte, vorzugsweise bereits kaltverformte, Draht bezeichnet. Vor der letzten Verformungsstufe in Form eines Walzenstiches ist das Erwärmungsaggregat 2 angeordnet. Der Walzvorgang durch nicht angetriebene Walzen ist durch das Walzgerüst 6 schematisch angedeutet. Nach dem Verlassen der letzten Verformungsstufe erfolgt die Abkühlung in einer analogen Abkühlvorrichtung 4, wie sie bereits in Fig.1 dargestellt wurde. Anschließend ist wiederum eine Vorrichtung 5 vorgesehen.In the illustration according to FIG. 2, the pre-rolled, preferably already cold-formed, wire is designated by 1. The heating unit 2 is arranged before the last deformation stage in the form of a roller pass. The rolling process by non-driven rolls is indicated schematically by the roll stand 6. After leaving the last deformation stage, cooling takes place in an analog cooling device 4, as has already been shown in FIG. A device 5 is then again provided.

Die Erfindung wird nachfolgend noch an Hand von Ausführungsbeispielen näher erläutert.The invention is explained in more detail below using exemplary embodiments.

Beispiel 1:Example 1:

Für die Herstellung von Spannbetondraht mit einem Durchmesser von 7 mm wurde ein vorgezogener Draht mit einem Durchmesser von 8,1 mm auf eine Temperatur von 320°C vor dem Eintritt in den letzten Ziehstein erwärmt. Bei dieser Temperatur wurde nachfolgend auf einen Durchmesser von 7,0 mm gezogen, wobei eine Temperatursteigerung von 80°C, ausgehend von 320° auf 400°C beobachtet wurde. Der Draht bestand aus unlegiertem Stahl mit einem Kohlenstoffgehalt von 0,83 Gew.% und einem Mangangehalt von 0,66 Gew.%. Nach der erfindungsgemäßen Behandlung wurde eine Zugfestigkeit von 1850 N/mm2 festgestellt. Vor der Behandlung hatte der Draht eine Zugfestigkeit von 1630 N/mm2.For the production of prestressed concrete wire with a diameter of 7 mm, a preferred wire with a diameter of 8.1 mm was heated to a temperature of 320 ° C. before entering the last drawing die. At this temperature, the diameter was subsequently drawn to 7.0 mm, an increase in temperature from 80 ° C. starting from 320 ° to 400 ° C. being observed. The wire consisted of unalloyed steel with a carbon content of 0.83% by weight and a manganese content of 0.66% by weight. After the treatment according to the invention, a tensile strength of 1850 N / mm 2 was found. Before the treatment, the wire had a tensile strength of 1630 N / mm 2 .

Die Relaxationsprüfung des erfindungsgemäß behandelten Materials unter einer Anfangslast von 70 % der Bruchlast ergab nach 1000 Stunden einen Spannungsabfall von 0,95 %.The relaxation test of the material treated according to the invention under an initial load of 70% of the breaking load showed a voltage drop of 0.95% after 1000 hours.

Vergleichsweise wurde mit dem gleichen Vormaterial, vorgezogener Draht mit einem Durchmesser von 8,1 mm und einer Zugfestigkeit von 1630 N/mm2, eine Behandlung nach dem Stand der Technik durchgeführt. Dabei wurde der Draht in üblicher Weise gezogen und anschließend der Behandlungstemperatur unterworfen, wonach sich eine Zugfestigkeit von 1740 N/mm2 einstellte.For comparison, a treatment according to the prior art was carried out with the same starting material, drawn wire with a diameter of 8.1 mm and a tensile strength of 1630 N / mm 2 . The wire was drawn in the usual way and then subjected to the treatment temperature, after which a tensile strength of 1740 N / mm 2 was established.

Beispiel 2:Example 2:

Für die Herstellung eines Stahldrahtes mit einem Durchmesser von 12 mm wurde ein vorgezogener Draht mit einem Durchmesser von 14 mm eingesetzt. Es handelte sich hier um einen unlegierten Stahl mit einem Kohlenstoffgehalt von 0,78 Gew.% und einem Mangangehalt von 0,75 Gew.%. Vor dem letzten Walzenstich wurde der Draht auf eine Temperatur von 400°C erwärmt. Beim Walzvorgang durch Schleppwalzen nahm die Temperatur um weitere 45°C auf 445°C zu. Die nach dieser Behandlung und Abkühlung gemessene Zugfestigkeit betrug 1690 N/mm2. Die Prüfung der Relaxation ergab nach 1000 Stunden einen Spannungsabfall von 1,2 %, gemessen an der Anfangslast von 70 % der Bruchlast.For the production of a steel wire with a diameter of 12 mm, a pre-drawn wire with a diameter of 14 mm was used. It was an unalloyed steel with a carbon content of 0.78% by weight and a manganese content of 0.75% by weight. Before the last roll pass, the wire was heated to a temperature of 400 ° C. During the rolling process by drag rolling, the temperature rose by a further 45 ° C to 445 ° C. The tensile strength measured after this treatment and cooling was 1690 N / mm 2 . The relaxation test showed a voltage drop of 1.2% after 1000 hours, measured on the initial load of 70% of the breaking load.

Je nach Stahlsorte werden beim erfindungsgemäßen Verfahren Behandlungstemperaturen zwischen 200°C und der Rekristallisationstemperatur des Stahles angewendet, wobei Verformungen bis 50 % Querschnittsabnahme, vorzugsweise 10 bis 35 %, zur Anwendung gelangen.Depending on the type of steel, treatment temperatures between 200 ° C. and the recrystallization temperature of the steel are used in the process according to the invention, deformations of up to 50% reduction in cross section, preferably 10 to 35%, being used.

Das erfindungsgemäße Verfahren eignet sich in erster Linie für die Behandlung von unlegierten Stahlsorten mit 0,30 bis 1,20 Gew.% Kohlenstoff oder für legierte Stähle mit bis zu 5 Gew.% Mangan und bis zu 3 Gew.% Silizium.The method according to the invention is primarily suitable for the treatment of unalloyed steel types with 0.30 to 1.20% by weight of carbon or for alloyed steels with up to 5% by weight of manganese and up to 3% by weight of silicon.

Claims (4)

1. Verfahren zur Herstellung von Stahldraht (1) mit hoher Zugfestigkeit und niedrigen Kriech-und Relaxationseigenschaften, bei welchem der Stahl einer Verformung und einer Wärmebehandlung unterzogen wird, dadurch gekennzeichnet, daß der Stahldraht (1) vor Eintritt in die letzte Verformungsstufe (4) auf eine gegenüber der für die Wärmebehandlung erforderlichen Temperatur geringere Temperatur erwärmt wird, welche zuzüglich der Verformungswärme bei einer Verformung von bis zu 50 % Querschnittsabnahme die gewünschte Behandlungstemperatur ergibt, und daß nach dieser Verformung der Stahldraht bei der Behandlungstemperatur gereckt wird.1. A process for the production of steel wire (1) with high tensile strength and low creep and relaxation properties, in which the steel is subjected to deformation and heat treatment, characterized in that the steel wire (1) before entering the last deformation step (4) is heated to a temperature which is lower than that required for the heat treatment, which plus the heat of deformation results in the desired treatment temperature in the case of a deformation of up to 50% reduction in cross-section, and that after this deformation the steel wire is stretched at the treatment temperature. 2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, daß die Wärmebehandlung bei Temperaturen zwischen 200°C und dem Ac,-Punkt, insbesondere 250°C bis 600°C, vorgenommen wird und daß die Erwärmung vor der letzten Verformungsstufe (4) im Falle der Verwendung von Ziehsteinen auf Temperaturen von 30°C bis 100°C unterhalb der gewünschten Wärmebehandlungstemperatur und im Fall der Verwendung von Walzen in der letzten Verformungsstufe (4) auf Temperaturen von 30°C bis 80°C unterhalb der gewünschten Wärmebehandlungstemperatur vorgenommen wird.2. The method according to claim 1, characterized in that the heat treatment at temperatures between 200 ° C and the Ac, point, in particular 250 ° C to 600 ° C, is carried out and that the heating before the last deformation stage (4) in the case the use of drawing dies at temperatures of 30 ° C to 100 ° C below the desired heat treatment temperature and in the case of the use of rollers in the last deformation step (4) to temperatures of 30 ° C to 80 ° C below the desired heat treatment temperature. 3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, daß die Verformung vorzugsweise mit 10 bis 40 % Querschnittsabnahme durchgeführt wird.3. The method according to claim 1 or 2, characterized in that the deformation is preferably carried out with 10 to 40% decrease in cross section. 4. Verfahren nach Anspruch 1, 2 oder 3, dadurch gekennzeichnet, daß unlegierte Stahlsorten mit 0,30 bis 1,20 Gew.% Kohlenstoff oder legierte Stähle mit bis zu 5 Gew.% Mangan und bis zu 3 Gew.% Silizium behandelt werden.4. The method according to claim 1, 2 or 3, characterized in that unalloyed steel with 0.30 to 1.20 wt.% Carbon or alloyed steels are treated with up to 5 wt.% Manganese and up to 3 wt.% Silicon .
EP86890113A 1985-04-26 1986-04-24 Process for manufacturing steel wire Withdrawn EP0199715A3 (en)

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AT1264/85 1985-04-26
AT126485A AT384564B (en) 1985-04-26 1985-04-26 METHOD FOR PRODUCING STEEL WIRE

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EP0199715A2 true EP0199715A2 (en) 1986-10-29
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US6508754B1 (en) 1997-09-23 2003-01-21 Interventional Therapies Source wire for radiation treatment
US6602228B2 (en) 1992-12-22 2003-08-05 Advanced Cardiovascular Systems, Inc. Method of soldering Ti containing alloys
US6682608B2 (en) 1990-12-18 2004-01-27 Advanced Cardiovascular Systems, Inc. Superelastic guiding member
US7918011B2 (en) 2000-12-27 2011-04-05 Abbott Cardiovascular Systems, Inc. Method for providing radiopaque nitinol alloys for medical devices
US7938843B2 (en) 2000-11-02 2011-05-10 Abbott Cardiovascular Systems Inc. Devices configured from heat shaped, strain hardened nickel-titanium
US7942892B2 (en) 2003-05-01 2011-05-17 Abbott Cardiovascular Systems Inc. Radiopaque nitinol embolic protection frame
US7976648B1 (en) 2000-11-02 2011-07-12 Abbott Cardiovascular Systems Inc. Heat treatment for cold worked nitinol to impart a shape setting capability without eventually developing stress-induced martensite

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US6682608B2 (en) 1990-12-18 2004-01-27 Advanced Cardiovascular Systems, Inc. Superelastic guiding member
US6461453B1 (en) 1990-12-18 2002-10-08 Advanced Cardiovascular Systems, Inc. Superelastic guiding member
US6592570B2 (en) 1990-12-18 2003-07-15 Advanced Cardiovascular Systems, Inc. Superelastic guiding member
US6638372B1 (en) 1990-12-18 2003-10-28 Advanced Cardiovascular Systems, Inc. Superelastic guiding member
US6165292A (en) * 1990-12-18 2000-12-26 Advanced Cardiovascular Systems, Inc. Superelastic guiding member
US7244319B2 (en) 1990-12-18 2007-07-17 Abbott Cardiovascular Systems Inc. Superelastic guiding member
US7258753B2 (en) 1990-12-18 2007-08-21 Abbott Cardiovascular Systems Inc. Superelastic guiding member
US6602228B2 (en) 1992-12-22 2003-08-05 Advanced Cardiovascular Systems, Inc. Method of soldering Ti containing alloys
US6508754B1 (en) 1997-09-23 2003-01-21 Interventional Therapies Source wire for radiation treatment
US7938843B2 (en) 2000-11-02 2011-05-10 Abbott Cardiovascular Systems Inc. Devices configured from heat shaped, strain hardened nickel-titanium
US7976648B1 (en) 2000-11-02 2011-07-12 Abbott Cardiovascular Systems Inc. Heat treatment for cold worked nitinol to impart a shape setting capability without eventually developing stress-induced martensite
US7918011B2 (en) 2000-12-27 2011-04-05 Abbott Cardiovascular Systems, Inc. Method for providing radiopaque nitinol alloys for medical devices
US7942892B2 (en) 2003-05-01 2011-05-17 Abbott Cardiovascular Systems Inc. Radiopaque nitinol embolic protection frame

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EP0199715A3 (en) 1987-09-30
AT384564B (en) 1987-12-10

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