EP0432434A1 - Process for manufacturing joining structural parts from a fully austenitic Cr-Mn steel. - Google Patents

Process for manufacturing joining structural parts from a fully austenitic Cr-Mn steel. Download PDF

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EP0432434A1
EP0432434A1 EP90120990A EP90120990A EP0432434A1 EP 0432434 A1 EP0432434 A1 EP 0432434A1 EP 90120990 A EP90120990 A EP 90120990A EP 90120990 A EP90120990 A EP 90120990A EP 0432434 A1 EP0432434 A1 EP 0432434A1
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steel
cold
diameter
product
production
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EP0432434B1 (en
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Gerald Stein
Marcus O. Speidel
Peter Uggowitzer
Joachim Menzel
Manfred Wagner
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Vereinigte Schmiedewerke GmbH
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Vereinigte Schmiedewerke GmbH
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N

Definitions

  • the invention relates to a method for producing products from a fully austenitic chromium-manganese steel and its use for connecting elements, in particular bolts, screws, nails, and for wire ropes.
  • AT-PS 337 235 relates to an austenitic stainless steel consisting of This steel is particularly suitable for highly stressed brackets, in motor-generator construction, for submarine cables and for the manufacture of pump housings. In the fully austenitic state, the steel can reach yield strength values of up to 1600 N / mm2 if it is reduced by 50%.
  • the steel has a chromium content of 15 to 27% and a manganese content of 21 to 30% according to a formula specified in the AT-PS. Since the steel is melted at atmospheric pressure, the high levels of chromium and manganese are necessary in order to increase the solubility limit of nitrogen in the steel accordingly when nitrogen carriers are added.
  • the austenitic nitrogen-containing steel melted according to the AT-PS is characterized by a low porosity. It has been shown, however, that such a steel cannot be brought to yield strengths above 1600 N / mm 2 by cold reduction with degrees of deformation above 50%. Experiments have shown that at higher degrees of cold reduction, for example when drawing primary material into thin wire cross sections, the material breaks. Porosity in the micro range was also observed. Apart from these metallurgical difficulties, such a steel is very expensive for large-scale use due to its high chromium and manganese content.
  • austenitic steels with 0.02 to 0.55% C, up to 2% Si, up to 20% Mn, 0 to 30% Cr, 0 to 25% Ni, 0 to 5 % Mo and / or V and more than 0.5%, preferably at least 1.4% nitrogen, which were melted under pressure in a nitrogen atmosphere, for the production of agitated, in particular to use machine parts subject to vibrations.
  • the object of the invention is to produce high-strength, corrosion-resistant objects.
  • the steels of the type according to the invention should be able to be cold worked almost indefinitely. For this purpose, they should be able to be machined from relatively high initial cross sections to the thinnest dimensions without the risk of breakage.
  • the required yield strength values of greater than 1800 N / mm2 can be achieved with certainty, in particular through the outsourcing of the end product preformed with the highest cross-sectional decreases at temperatures of 300 to 500 ° C. for a time of 20 minutes to 5, adapted to the cross section Hours.
  • This aging treatment results in a rearrangement of the dislocations within the steel formed during the previous cold forming processes, and without changing the so-called dislocation density, which is ultimately responsible for the high strength of these steels.
  • the steels produced according to the invention as connecting elements, such as bolts, screws, nails or as wire ropes, require the inner structure of the steels thus created that very high internal stresses have to be used for further deformation. However, this means that the steels can withstand the highest loads when they are used later.
  • An independent variant for solving the problem according to the invention consists in the use of powder instead of a cast product as the starting material according to claim 2.
  • the metal powder is shaped by hot isostatic pressing to form a billet, which is then forged and / or rolled out to a precursor of 5 to 150 mm in diameter is, the preliminary product is then cold-formed with a cross-sectional decrease of at least 60% to an end product with a diameter of 0.5 to 90 mm and then the end product is aged at temperatures of 300 to 500 ° C. for a period of 20 minutes to 5 hours.
  • Connection elements in particular bolts, screws, nails and wire ropes, are preferably produced by the method according to the invention.
  • the steel block solidified in the pressure electroslag remelting furnace with the above overall analysis was then brought to a cross section of 7 mm in diameter by forging and rolling.
  • the diameter was cold drawn from 7 mm to 3 mm in 8 passes. This corresponds to a total deformation of 82% (approx. 10% cold deformation per train).
  • the wire was further cold drawn from a diameter of 3 mm to 1.8 mm.
  • the total deformation was 64% in 6 moves (approx. 10% deformation per move).
  • the wire drawn to a diameter of 1.8 mm was then aged at a temperature of 400 ° C. for 4 hours.
  • the corresponding values before the aging treatment were 2100 N / mm2 for the yield strength, 2220 N / mm2 for the tensile strength, 6% for the elongation and 46% for the fracture constriction.
  • the aging treatment according to the invention is of high importance. With this aging treatment it is possible to set yield strengths and tensile strength values that were previously unknown. It is particularly surprising that the values for the toughness, expressed here by the elongation and the constriction of the fracture, remain constant.
  • the steels remain non-magnetic even at the highest degrees of deformation. It also reduces susceptibility to stress corrosion cracking in dilute aqueous solutions up to 80 ° C.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Forging (AREA)
  • Powder Metallurgy (AREA)

Abstract

The invention relates to the processes for the production of a corrosion-resistant fully austenitic steel containing, in % by weight: max. 0.12% of C 0.20 to 1.00% of Si 17.50 to 20.00% of Mn max. 0.05% of P max. 0.015% of S 17.50 to 20.00% of Cr max. 5.00% of Mo max. 3.00% of Ni 0.80 to 1.20% of N, the remainder being iron and conventional impurities from the smelting process, in which an electrode is produced for electroslag remelting, the nitrogen content of the steel is adjusted in a pressure electroslag remelting process with melting of this electrode for the addition of nitrogen-containing materials, the steel block solidifying under pressure is then drawn out and/or rolled out to an intermediate product of 5 to 150 mm diameter, the intermediate product is then cold-worked with a reduction in total cross-section of at least 60% to give an end product of 0.5 to 90 mm diameter and the end product is then aged at temperatures of 300 to 500 DEG C for 20 minutes to 5 hours.

Description

Die Erfindung betrifft ein Verfahren zur Herstellung von Erzeugnissen aus einem vollaustenitischen Chrom-Mangan-Stahl und seine Verwendung für Verbindungselemente, insbesondere Bolzen, Schrauben, Nägel, und für Drahtseile.The invention relates to a method for producing products from a fully austenitic chromium-manganese steel and its use for connecting elements, in particular bolts, screws, nails, and for wire ropes.

Die AT-PS 337 235 betrifft einen austenitischen rostfreien Stahl, bestehend aus

Figure imgb0001
Dieser Stahl eignet sich besonders vorteilhaft für hochbeanspruchte Halterungen, im Motor-Generatorbau, für Unterseekabel und zur Herstellung von Pumpengehäusen. Der Stahl kann im vollaustenitischen Zustand Streckgrenzenwerte bis 1600 N/mm² erreichen, wenn er bis 50 % kaltreduziert wird.AT-PS 337 235 relates to an austenitic stainless steel consisting of
Figure imgb0001
 This steel is particularly suitable for highly stressed brackets, in motor-generator construction, for submarine cables and for the manufacture of pump housings. In the fully austenitic state, the steel can reach yield strength values of up to 1600 N / mm² if it is reduced by 50%.

Voraussetzung für das Erreichen solch hoher Streckgrenzenwerte ist jedoch, daß der Stahl nach einer in der AT-PS festgelegten Formel Chromgehalte von 15 bis 27 % sowie Mangangehalte von 21 bis 30 % aufweist. Da der Stahl bei Atmosphärendruck erschmolzen wird, sind die hohen Gehalte an Chrom und Mangan erforderlich, um die Löslichkeitsgrenze des Stickstoffs im Stahl bei Zugabe von Stickstoffträgern entsprechend zu erhöhen. Der nach der AT-PS erschmolzene austenitische stickstoffhaltige Stahl zeichnet sich zwar durch eine geringe Porosität aus. Es hat sich jedoch gezeigt, daß ein solcher Stahl nicht durch Kaltreduzieren mit Verformungsgraden oberhalb 50 % auf über 1600 N/mm² liegende Streckgrenzenwerte gebracht werden kann. Versuche haben ergeben, daß bei höheren Kaltreduktionsgraden, beispielsweise beim Ziehen von Vormaterial zu dünnen Drahtquerschnitten, das Material bricht. Außerdem wurde Porosität im Mikrobereich beobachtet. Abgesehen von diesen metallurgischen Schwierigkeiten ist ein solcher Stahl für den großtechnischen Einsatz infolge seiner hohen Chrom- und Mangangehalte sehr teuer.Prerequisite for reaching such high Yield strength values, however, are that the steel has a chromium content of 15 to 27% and a manganese content of 21 to 30% according to a formula specified in the AT-PS. Since the steel is melted at atmospheric pressure, the high levels of chromium and manganese are necessary in order to increase the solubility limit of nitrogen in the steel accordingly when nitrogen carriers are added. The austenitic nitrogen-containing steel melted according to the AT-PS is characterized by a low porosity. It has been shown, however, that such a steel cannot be brought to yield strengths above 1600 N / mm 2 by cold reduction with degrees of deformation above 50%. Experiments have shown that at higher degrees of cold reduction, for example when drawing primary material into thin wire cross sections, the material breaks. Porosity in the micro range was also observed. Apart from these metallurgical difficulties, such a steel is very expensive for large-scale use due to its high chromium and manganese content.

Wie in der AT-PS weiterhin ausgeführt, ist es zwar möglich, die nachteilige Porosität durch ein Erschmelzen der hier in Rede stehenden Chrom-Mangan-Stickstoff-Stähle unter erhöhtem Druck weitgehend zu verhindern. Bei diesen bekannten Verfahren können jedoch nur Maximalstickstoffgehalte von 0,8 Gew.-% erzielt werden. Diese Stickstoffgehalte reichen jedoch nicht aus, um Festigkeitswerte größer 1600 N/mm² zu erzielen.As further stated in the AT-PS, it is possible to largely prevent the disadvantageous porosity by melting the chrome-manganese-nitrogen steels in question here under increased pressure. With these known methods, however, only a maximum nitrogen content of 0.8% by weight can be achieved. However, these nitrogen contents are not sufficient to achieve strength values greater than 1600 N / mm².

Weiterhin ist es aus der AT-PS 266 900 bekannt, austenitische Stähle mit 0,02 bis 0,55 % C, bis 2 % Si, bis 20 % Mn, 0 bis 30 % Cr, 0 bis 25 % Ni, 0 bis 5 % Mo und/oder V und mehr als 0,5 %, vorzugsweise mindestens 1,4 % Stickstoff, die in Stickstoffatmosphäre unter Druck erschmolzen wurden, zur Herstellung von bewegten, insbesondere schwingend beanspruchten Maschinenteilen zu verwenden.Furthermore, it is known from AT-PS 266 900, austenitic steels with 0.02 to 0.55% C, up to 2% Si, up to 20% Mn, 0 to 30% Cr, 0 to 25% Ni, 0 to 5 % Mo and / or V and more than 0.5%, preferably at least 1.4% nitrogen, which were melted under pressure in a nitrogen atmosphere, for the production of agitated, in particular to use machine parts subject to vibrations.

Diese bekannten Stähle sollen im abgeschreckten Zustand Dauerfestigkeiten bis 100 Kp/mm² erreichen.These known steels are said to achieve fatigue strengths of up to 100 Kp / mm² in the quenched state.

Aufgabe der Erfindung ist die Erzeugung hochfester korrosionsbeständiger Gegenstände. Dabei sollen sich die Stähle der erfindungsgemäßen Art nahezu unbegrenzt kaltverformen lassen. Sie sollen dazu von relativ hohen Ausgangsquerschnitten bis zu dünnsten Abmessungen ohne Bruchgefahr heruntergearbeitet werden können.The object of the invention is to produce high-strength, corrosion-resistant objects. The steels of the type according to the invention should be able to be cold worked almost indefinitely. For this purpose, they should be able to be machined from relatively high initial cross sections to the thinnest dimensions without the risk of breakage.

Es hat sich gezeigt, daß die Analyseneinstellung im beanspruchten Bereich in Verbindung mit dem an sich bekannten Druckelektroschlackeumschmelzverfahren und der nach dem Kaltumformen erfolgenden Auslagerung zu höchsten Streckgrenzenwerten über 1800 N/mm² führt. Dabei ist der Stahl gleichzeitig auch porenfrei. Verformungsgrade (=Ausgangsquerschnitt-Endquerschnitt:Ausgangsquerschnittx100 %) bis 90 % sind möglich, weil die hohen Streckgrenzenwerte erst nach dem abschließenden Auslagern erzielt werden.It has been shown that the analysis setting in the claimed range in conjunction with the known pressure electro-slag remelting process and the aging after cold forming leads to the highest yield strength values over 1800 N / mm². The steel is also non-porous at the same time. Degrees of deformation (= initial cross-sectional end cross-section: initial cross-section x100%) to 90% are possible because the high yield strength values are only achieved after the final outsourcing.

Mit dem erfindungsgemäßen Verfahren lassen sich die geforderten Streckgrenzenwerte von größer 1800 N/mm² mit Sicherheit erreichen, insbesondere durch das erfindungsgemäß vorgesehene Auslagern des mit höchsten Querschnittsabnahmen vorverformten Endprodukts bei Temperaturen von 300 bis 500 °C für eine dem Querschnitt angepaßte Zeit von 20 Minuten bis 5 Stunden. Diese Auslagerungsbehandlung bedingt eine Umordnung der bei den vorherigen Kaltverformungsvorgängen gebildeten Versetzungen innerhalb des Stahls, und zwar ohne Änderung der sog. Versetzungsdichte, die letztendlich für die hohe Festigkeit dieser Stähle verantwortlich ist. Beim späteren Einsatz der erfindungsgemäß hergestellten Stähle als Verbindungselemente, wie Bolzen, Schrauben, Nägel oder als Drahtseile, bedingt die so geschaffene innere Struktur der Stähle, daß zur weiteren Verformung sehr hohe innere Spannungen aufgewendet werden müssen. Das bedeutet aber, daß die Stähle bei ihrem späteren Einsatz höchsten Belastungen gewachsen sind.With the method according to the invention, the required yield strength values of greater than 1800 N / mm² can be achieved with certainty, in particular through the outsourcing of the end product preformed with the highest cross-sectional decreases at temperatures of 300 to 500 ° C. for a time of 20 minutes to 5, adapted to the cross section Hours. This aging treatment results in a rearrangement of the dislocations within the steel formed during the previous cold forming processes, and without changing the so-called dislocation density, which is ultimately responsible for the high strength of these steels. Later use The steels produced according to the invention as connecting elements, such as bolts, screws, nails or as wire ropes, require the inner structure of the steels thus created that very high internal stresses have to be used for further deformation. However, this means that the steels can withstand the highest loads when they are used later.

Eine eigenständige Variante zur Lösung des erfindungsgemäßen Problems besteht in dem Einsatz von Pulver anstelle eines Gußprodukts als Ausgangsmaterial gemäß Anspruch 2. Das Metallpulver wird durch heißisostatisches Verpressen zu einem Vorblock geformt, der dann zu einem Vorprodukt von 5 bis 150 mm Durchmesser umgeschmiedet und/oder ausgewalzt wird, das Vorprodukt dann mit einer Querschnittsabnahme von mindestens 60 % zu einem Endprodukt mit 0,5 bis 90 mm Durchmesser kaltverformt wird und anschließend das Endprodukt bei Temperaturen von 300 bis 500 °C für eine Zeit von 20 Minuten bis 5 Stunden ausgelagert wird.An independent variant for solving the problem according to the invention consists in the use of powder instead of a cast product as the starting material according to claim 2. The metal powder is shaped by hot isostatic pressing to form a billet, which is then forged and / or rolled out to a precursor of 5 to 150 mm in diameter is, the preliminary product is then cold-formed with a cross-sectional decrease of at least 60% to an end product with a diameter of 0.5 to 90 mm and then the end product is aged at temperatures of 300 to 500 ° C. for a period of 20 minutes to 5 hours.

Die Herstellung des Stahls auf pulvermetallurgischem Wege bietet eine ausgezeichnete Garantie für einen hervorragenden Reinheitsgrad und das Nichtvorliegen von Porosität.The production of the steel by powder metallurgy offers an excellent guarantee for an excellent degree of purity and the absence of porosity.

Bevorzugt werden nach dem erfindungsgemäßen Verfahren Verbindungselemente, insbesondere Bolzen, Schrauben, Nägel, sowie Drahtseile, erzeugt.Connection elements, in particular bolts, screws, nails and wire ropes, are preferably produced by the method according to the invention.

Anhand der folgenden Beispiele wird die Erfindung erläutert.The invention is illustrated by the following examples.

In einem Druckelektroschlackeumschmelzofen wurde eine Elektrode der folgenden Zusammensetzung (in Masse-%)

Figure imgb0002
In a pressure electroslag remelting furnace, an electrode of the following composition (in mass%)
Figure imgb0002

Der im Druckelektroschlackeumschmelzofen erstarrte Stahlblock mit der obigen Gesamtanalyse wurde dann durch Schmieden und Walzen auf einen Querschnitt von 7 mm Durchmesser gebracht. In 8 Zügen wurde der Durchmesser von 7 mm auf 3 mm kaltgezogen. Dies entspricht einer Gesamtverformung von 82 % (ca. 10 % Kaltverformung pro Zug).The steel block solidified in the pressure electroslag remelting furnace with the above overall analysis was then brought to a cross section of 7 mm in diameter by forging and rolling. The diameter was cold drawn from 7 mm to 3 mm in 8 passes. This corresponds to a total deformation of 82% (approx. 10% cold deformation per train).

Nach einer Zwischenglühung bei 1080 °C wurde der Draht weiter kaltgezogen vom Durchmesser 3 mm auf 1,8 mm. Die Gesamtumformung betrug dabei 64 % in 6 Zügen (ca. 10 % Verformung pro Zug). Anschließend wurde der auf 1,8 mm Durchmesser gezogene Draht bei einer Temperatur von 400 °C für 4 Stunden ausgelagert.After intermediate annealing at 1080 ° C, the wire was further cold drawn from a diameter of 3 mm to 1.8 mm. The total deformation was 64% in 6 moves (approx. 10% deformation per move). The wire drawn to a diameter of 1.8 mm was then aged at a temperature of 400 ° C. for 4 hours.

Danach wurde eine Streckgrenze von Rp = 2400 N/mm² , eine Zugfestigkeit Rm von 2550 N/mm² , ein Dehnung A = 6,1 % und eine Brucheinschnürung Z von 48,3 % im Rahmen des üblichen Zugversuches ermittelt.Then a yield strength of Rp = 2400 N / mm², a tensile strength Rm of 2550 N / mm², an elongation A = 6.1% and a fracture necking Z of 48.3% were determined in the course of the usual tensile test.

Die entsprechenden Werte vor der Auslagerungsbehandlung betrugen für die Streckgrenze 2100 N/mm² , für die Zugfestigkeit 2220 N/mm² , für die Dehnung 6 % und für die Brucheinschnürung 46 %.The corresponding values before the aging treatment were 2100 N / mm² for the yield strength, 2220 N / mm² for the tensile strength, 6% for the elongation and 46% for the fracture constriction.

Daraus erhellt, daß in bezug auf die gewünschte Steigerung der Festigkeitswerte der erfindungsgemäßen Auslagerungsbehandlung ein hoher Stellenwert beizumessen ist. Gelingt es doch mit dieser Auslagerungsbehandlung, Streckgrenzen- und Zugfestigkeitswerte einzustellen, wie sie bisher noch nicht bekannt waren. Dabei ist insbesondere überraschend, daß die Werte für die Zähigkeit, hier ausgedrückt durch die Dehnung und die Brucheinschnürung, konstant bleiben.It is evident from this that, in relation to the desired increase in the strength values, the aging treatment according to the invention is of high importance. With this aging treatment it is possible to set yield strengths and tensile strength values that were previously unknown. It is particularly surprising that the values for the toughness, expressed here by the elongation and the constriction of the fracture, remain constant.

Es hat sich weiterhin bei den Versuchen gezeigt, daß auch bei sehr hohen Kaltverformungsgraden das austenitische Gefüge durch den hohen Stickstoffgehalt und den hohen Reinheitsgrad so stabilisiert ist, daß ein Umklappen des Austenits in Martensit nicht auftrat. Damit können die bisher bei austenitischen Stählen beobachteten schädlichen Wirkungen des sog. Verformungs-Martensits vermieden werden, insbesondere ein Abfall der Zähigkeit, was ein Ende der Kaltziehfähigkeit bedeutet.It has also been shown in the tests that, even at very high degrees of cold deformation, the austenitic structure is so stabilized by the high nitrogen content and the high degree of purity that the austenite did not fold over into martensite. The harmful effects of the so-called deformation martensite previously observed in austenitic steels can thus be avoided, in particular a drop in toughness, which means an end to the cold drawing ability.

Ferner bleiben die Stähle auch bei höchsten Verformungsgraden unmagnetisch. Außerdem wird die Anfälligkeit gegen Spannungsrißkorrosion in verdünnten wässrigen Lösungen bis 80 °C verringert.Furthermore, the steels remain non-magnetic even at the highest degrees of deformation. It also reduces susceptibility to stress corrosion cracking in dilute aqueous solutions up to 80 ° C.

Claims (8)

Verfahren zur Herstellung von Erzeugnissen aus einem vollaustenitischen Chrom-Mangan-Stahl mit (in Masse-%):
Figure imgb0003
Rest Eisen und übliche erschmelzungsbedingte Verunreinigungen, bei dem eine Elektrode für das Elektroschlackeumschmelzen erzeugt wird, der Stickstoffgehalt des Stahls in einem Druckelektroschlacke umschmelzverfahren beim Abschmelzen dieser Elektrode durch Zugabe von stickstoffhaltigen Materialien eingestellt wird, der unter Druck erstarrte Stahlblock dann zu einem Vorprodukt von 5 bis 150 mm Durchmesser ausgeschmiedet und/oder ausgewalzt wird, das Vorprodukt anschließend mit einer Gesamtquerschnittsabnahme von mindestens 60 % zu einem Endprodukt mit 0,5 bis 90 mm Durchmesser kaltverformt wird, worauf das Endprodukt bei Temperaturen von 300 bis 500 °C für 20 Minuten bis 5 Stunden ausgelagert wird.Process for the production of products from a fully austenitic chrome-manganese steel with (in mass%):
Figure imgb0003
Remainder iron and usual smelting-related impurities, in which an electrode for the electroslag remelting is produced, the nitrogen content of the steel in a pressure electroslag remelting process is adjusted when this electrode is smelted by adding nitrogen-containing materials, the steel block which has solidified under pressure then becomes a preliminary product of 5 to 150 mm diameter is forged and / or rolled out, the preliminary product is then cold-formed with a total cross-sectional decrease of at least 60% to an end product with a diameter of 0.5 to 90 mm, whereupon the end product at temperatures of 300 to 500 ° C for 20 minutes to 5 hours is outsourced. Verfahren zur Herstellung von Erzeugnissen aus einem vollaustenitischen Stahl mit (in Masse-%):
Figure imgb0004
Rest Eisen und übliche erschmelzungsbedingte Verunreinigungen, bei dem ein Metallpulver erzeugt wird, der Stickstoffstoffgehalt durch Aufsticken des Metallpulvers in fester Phase eingestellt wird, das Metallpulver durch heißisostatisches Pressen zu einem Vorblock geformt wird, dieser Vorblock dann zu einem Vorprodukt von 5 bis 150 mm Durchmesser ausgeschmiedet und/oder ausgewalzt wird, das Vorprodukt dann mit einer Gesamtquerschnittsabnahme von mindestens 60 % zu einem Endprodukt mit 0,5 bis 90 mm Durchmesser kaltverformt wird, und anschließend das Endprodukt bei Temperaturen von 300 bis 500 °C für eine Zeit von 20 Minuten bis 5 Stunden ausgelagert wird.Process for the production of products from a fully austenitic steel with (in mass%):
Figure imgb0004
Remainder iron and usual melting-related impurities, in which a metal powder is produced, the nitrogen content is adjusted by embroidering the metal powder in the solid phase, the metal powder is shaped into a billet by hot isostatic pressing, this billet is then forged into a billet of 5 to 150 mm in diameter and / or is rolled out, the preliminary product is then cold-formed with an overall cross-sectional decrease of at least 60% to an end product with a diameter of 0.5 to 90 mm, and then the end product at temperatures of 300 to 500 ° C. for a period of 20 minutes to 5 Hours is outsourced. Verfahren nach Anspruch 1 oder 2,
dadurch gekennzeichnet, daß das Vorprodukt durch Recken kalt verformt wird.Method according to claim 1 or 2,
characterized in that the preliminary product is cold-formed by stretching. Verfahren nach Anspruch 1 oder 2,
dadurch gekennzeichnet, daß das Vorprodukt durch Ziehen kalt verformt wird.Method according to claim 1 or 2,
characterized in that the preliminary product is cold-formed by drawing. Verfahren nach Anspruch 4,
dadurch gekennzeichnet, daß das Ziehen in mehreren Teilschritten erfolgt.Method according to claim 4,
characterized in that the pulling takes place in several substeps. Verfahren nach den Ansprüchen 4 oder 5,
dadurch gekennzeichnet, daß nach dem ersten Ziehschritt ein Zwischenglühen bei Temperaturen von 1000 bis 1150 °C vorgenommen wird.Method according to claims 4 or 5,
characterized in that an intermediate annealing is carried out at temperatures of 1000 to 1150 ° C after the first drawing step. Verwendung eines nach einem der Ansprüche 1 bis 6 hergestellten Stahls als Werkstoff zur Herstellung von Verbindungselementen, insbesondere Bolzen, Schrauben, Nägel, mit einer Mindeststreckgrenze von 1800 N/mm².Use of a steel produced according to one of claims 1 to 6 as a material for the production of connecting elements, in particular bolts, screws, nails, with a minimum yield strength of 1800 N / mm². Verwendung eines nach einem der Ansprüche 1 bis 6 hergestellten Stahls als Werkstoff zur Herstellung von Drahtseilen mit einer Mindeststreckgrenze von 1800 N/mm².Use of a steel produced according to one of claims 1 to 6 as a material for the production of wire ropes with a minimum yield strength of 1800 N / mm².
EP90120990A 1989-12-07 1990-11-02 Process for manufacturing joining structural parts from a fully austenitic Cr-Mn steel. Expired - Lifetime EP0432434B1 (en)

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DE3940438 1989-12-07
DE3940438A DE3940438C1 (en) 1989-12-07 1989-12-07

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Cited By (10)

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WO1998048070A1 (en) * 1997-04-22 1998-10-29 Krupp Vdm Gmbh High-strength, anti-corrosive iron-manganese-chrome alloy
EP0918099A1 (en) * 1997-10-27 1999-05-26 Stahlwerk Ergste Westig GmbH Chrome-manganese steel alloy
WO1999031282A1 (en) * 1997-12-17 1999-06-24 Haldex Garphyttan Aktiebolag Cold drawn wire and method for the manufacturing of such wire
EP1069202A1 (en) * 1999-07-15 2001-01-17 Schoeller-Bleckmann Oilfield Technology GmbH & Co KG A paramagnetic, corrosion resistant austenitic steel with high elasticity, strength and toughness and a process for its manufacture
US6331772B1 (en) 1996-11-22 2001-12-18 Daimlerchrysler Ag Sensor component
US6682581B1 (en) 1999-05-26 2004-01-27 Basf Aktiengesellschaft Nickel-poor austenitic steel
US6682582B1 (en) 1999-06-24 2004-01-27 Basf Aktiengesellschaft Nickel-poor austenitic steel
EP1538232A1 (en) * 2003-12-03 2005-06-08 BÖHLER Edelstahl GmbH Corrosion resistant austenitic steel.
EP1795619A3 (en) * 2005-12-06 2009-04-08 Teufelberger Seil Gesellschaft m.b.h. Manganese bearing steel wire for linear traction transmission element and process for manufacturing and use thereof
CN105220067A (en) * 2014-06-11 2016-01-06 丹阳市凯鑫合金材料有限公司 The resonant rod of the radio-frequency (RF) device production method of invar cold-heading silk

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DE19607828C2 (en) * 1995-04-15 2003-06-18 Vsg En Und Schmiedetechnik Gmb Process for producing an austenitic Cv-Mn steel
US7658883B2 (en) 2006-12-18 2010-02-09 Schlumberger Technology Corporation Interstitially strengthened high carbon and high nitrogen austenitic alloys, oilfield apparatus comprising same, and methods of making and using same
JP5858424B2 (en) * 2011-12-01 2016-02-10 株式会社日本製鋼所 Stainless steel for polymer electrolyte fuel cell separator and method for producing the same
CN102719682B (en) * 2012-02-14 2014-05-21 攀钢集团江油长城特殊钢有限公司 Smelting method of GH901 alloy
JP6640654B2 (en) * 2016-05-30 2020-02-05 株式会社東芝 Manufacturing method of high Cr steel parts
DE102017116615B3 (en) 2017-07-24 2018-08-30 Benteler Steel/Tube Gmbh Piston cylinder system with at least one pipe element
CN111500942B (en) * 2020-05-11 2021-08-10 湖南恒基粉末科技有限责任公司 High-nitrogen-content non-magnetic stainless steel powder and preparation method thereof
CN112719794B (en) * 2020-12-16 2022-03-11 浙江福尔加机械股份有限公司 Machining method of automobile hub bolt

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Cited By (23)

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Publication number Priority date Publication date Assignee Title
US6331772B1 (en) 1996-11-22 2001-12-18 Daimlerchrysler Ag Sensor component
WO1998048070A1 (en) * 1997-04-22 1998-10-29 Krupp Vdm Gmbh High-strength, anti-corrosive iron-manganese-chrome alloy
EP0918099A1 (en) * 1997-10-27 1999-05-26 Stahlwerk Ergste Westig GmbH Chrome-manganese steel alloy
WO1999031282A1 (en) * 1997-12-17 1999-06-24 Haldex Garphyttan Aktiebolag Cold drawn wire and method for the manufacturing of such wire
US6383316B1 (en) 1997-12-17 2002-05-07 Haldex Garphyttan Aktiebolag Cold drawn wire and method for the manufacturing of such wire
US6682581B1 (en) 1999-05-26 2004-01-27 Basf Aktiengesellschaft Nickel-poor austenitic steel
US6682582B1 (en) 1999-06-24 2004-01-27 Basf Aktiengesellschaft Nickel-poor austenitic steel
US6454879B1 (en) 1999-07-15 2002-09-24 Schoeller-Bleckman Oilfield Technology Gmbh & Co. Kg Process for producing a paramagnetic, corrosion-resistant material and like materials with high yield strength, strength, and ductility
EP1069202A1 (en) * 1999-07-15 2001-01-17 Schoeller-Bleckmann Oilfield Technology GmbH & Co KG A paramagnetic, corrosion resistant austenitic steel with high elasticity, strength and toughness and a process for its manufacture
NO340359B1 (en) * 2003-12-03 2017-04-10 Boehler Edelstahl Corrosion-resistant, austenitic steel alloy
EP1538232A1 (en) * 2003-12-03 2005-06-08 BÖHLER Edelstahl GmbH Corrosion resistant austenitic steel.
US7708841B2 (en) 2003-12-03 2010-05-04 Boehler Edelstahl Gmbh & Co Kg Component for use in oil field technology made of a material which comprises a corrosion-resistant austenitic steel alloy
US7947136B2 (en) 2003-12-03 2011-05-24 Boehler Edelstahl Gmbh & Co Kg Process for producing a corrosion-resistant austenitic alloy component
US8454765B2 (en) 2003-12-03 2013-06-04 Boehler Edelstahl Gmbh & Co. Kg Corrosion-resistant austenitic steel alloy
EP1795619A3 (en) * 2005-12-06 2009-04-08 Teufelberger Seil Gesellschaft m.b.h. Manganese bearing steel wire for linear traction transmission element and process for manufacturing and use thereof
CN105220067B (en) * 2014-06-11 2017-03-01 丹阳市凯鑫合金材料有限公司 The resonant rod of the radio-frequency (RF) device production method of invar cold-heading silk
CN105220067A (en) * 2014-06-11 2016-01-06 丹阳市凯鑫合金材料有限公司 The resonant rod of the radio-frequency (RF) device production method of invar cold-heading silk
CN106834950A (en) * 2014-06-11 2017-06-13 丹阳市凯鑫合金材料有限公司 A kind of production method of invar cold-heading silk
CN106834951A (en) * 2014-06-11 2017-06-13 丹阳市凯鑫合金材料有限公司 A kind of resonant rod of RF device invar cold-heading silk
CN106893936A (en) * 2014-06-11 2017-06-27 丹阳市凯鑫合金材料有限公司 Using the resonant rod invar cold-heading silk of vacuum melting and electroslag remelting operation
CN106893937A (en) * 2014-06-11 2017-06-27 丹阳市凯鑫合金材料有限公司 Using the resonant rod invar cold-heading silk of vacuum melting and electroslag remelting operation
CN106893937B (en) * 2014-06-11 2018-11-27 丹阳市凯鑫合金材料有限公司 Using the resonant rod of vacuum melting and electroslag remelting process invar cold-heading silk
CN106893936B (en) * 2014-06-11 2018-11-30 丹阳市凯鑫合金材料有限公司 The production method of the resonant rod of the RF device of vacuum melting invar cold-heading silk

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ATE111968T1 (en) 1994-10-15
DE59007249D1 (en) 1994-10-27
JPH0688160A (en) 1994-03-29
EP0432434B1 (en) 1994-09-21
DE3940438C1 (en) 1991-05-23

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