EP1918401B1 - Steel alloy for machining tools - Google Patents

Steel alloy for machining tools Download PDF

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Publication number
EP1918401B1
EP1918401B1 EP07450174.3A EP07450174A EP1918401B1 EP 1918401 B1 EP1918401 B1 EP 1918401B1 EP 07450174 A EP07450174 A EP 07450174A EP 1918401 B1 EP1918401 B1 EP 1918401B1
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Prior art keywords
steel alloy
weight
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leg
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German (de)
French (fr)
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EP1918401A2 (en
EP1918401A3 (en
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Ernst Putzgruber
Devrim Caliskanoglu
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Voestalpine Boehler Edelstahl GmbH and Co KG
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Boehler Edelstahl GmbH and Co KG
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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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/18—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for knives, scythes, scissors, or like hand cutting tools
    • 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
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the invention relates to a steel alloy for cutting tools.
  • the cutting area of the tool is charged several times high.
  • the tool material must, in order to withstand the total load, at the same time have high hardness and toughness as well as the like abrasion resistance, which properties are to be maintained up to high temperatures, for example 550 ° C and above. Only such a long service life of the tool and an economical use of the same can be achieved.
  • a load better explained the profile of a load, a cutting edge region of a tool during cutting or during a chip removal depends essentially on the nature and properties of the workpiece material.
  • high speed steels with different chemical compositions in particular adapted to the specific stresses in the chip removal of workpieces with different properties have been developed and are state of the art.
  • High speed steels however, have predominantly high levels of one or more expensive alloying elements such as molybdenum, tungsten, vanadium, niobium, and cobalt.
  • Tungsten and / or molybdenum may be provided to levels of 20% by weight and higher, with vanadium being alloyed in standard PM high speed steels at levels of 1.2 to 15% by weight.
  • a steel for low cost cutting tools for alloying elements is disclosed AT 412 285 B .
  • This steel which can be advantageously used in particular for circular saws, uses a specific aluminum-to-nitrogen ratio in order to minimize chip wear on the tool.
  • saw teeth usually work at lower temperatures during chip removal, so that in most cases no pronounced tempering temperature resistance of the material is required.
  • the invention now aims to provide a steel for cutting tools, which has a fine solidification structure and a good hot workability, has a high hardness acceptance and tempering resistance and shows high efficiency and a favorable price-performance ratio.
  • composition of the steel alloy according to the invention has metallurgical advantages that are synergistically limited to a narrow concentration range of the alloying elements.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)

Description

Die Erfindung bezieht sich auf eine Stahllegierung für spanabhebende Werkzeuge.The invention relates to a steel alloy for cutting tools.

Bei einer Spanabnahme von Werkstücken wird der Schneidenbereich des Werkzeuges mehrfach hoch belastet. Der Werkzeugwerkstoff muss, um der Summenbelastung zu widerstehen, gleichzeitig hohe Härte und Zähigkeit sowie dgl. Abriebfestigkeit aufweisen, welche Eigenschaften bis zu hohen Temperaturen, beispielsweise 550°C und darüber erhalten bleiben sollen. Nur derart sind hohe Standzeiten des Werkzeuges und ein wirtschaftlicher Einsatz desselben erreichbar.When a chip removal of workpieces, the cutting area of the tool is charged several times high. The tool material must, in order to withstand the total load, at the same time have high hardness and toughness as well as the like abrasion resistance, which properties are to be maintained up to high temperatures, for example 550 ° C and above. Only such a long service life of the tool and an economical use of the same can be achieved.

Eine Belastung, besser dargelegt das Profil einer Belastung, eines Schneidkantenbereiches eines Werkzeuges beim Schnitt bzw. bei einer Abspanung hängt wesentlich von der Art und den Eigenschaften des Werkstückswerkstoffes ab. So wurden beispielsweise Schnellarbeitsstähle mit unterschiedlichen chemischen Zusammensetzungen, insbesondere abgestimmt auf die spezifischen Beanspruchungen bei der Spanabnahme von Werkstücken mit unterschiedlichen Eigenschaften entwickelt und zählen zum Stand der Technik.A load, better explained the profile of a load, a cutting edge region of a tool during cutting or during a chip removal depends essentially on the nature and properties of the workpiece material. Thus, for example, high speed steels with different chemical compositions, in particular adapted to the specific stresses in the chip removal of workpieces with different properties have been developed and are state of the art.

Schnellarbeitsstähle weisen allerdings vorwiegend hohe Gehalte an einem oder mehreren teuren Legierungselementen wie Molybdän, Wolfram, Vanadin, Niob und Kobalt auf. Wolfram und/oder Molybdän können bis zu Gehalten von 20 Gew.-% und höher vorgesehen sein, wobei Vanadin in üblichen PM-Schnellstählen mit Gehalten von 1.2 bis 15 Gew.-% zulegiert sein kann.High speed steels, however, have predominantly high levels of one or more expensive alloying elements such as molybdenum, tungsten, vanadium, niobium, and cobalt. Tungsten and / or molybdenum may be provided to levels of 20% by weight and higher, with vanadium being alloyed in standard PM high speed steels at levels of 1.2 to 15% by weight.

Wie vorher mittels einer PM-Erzeugungsvariante angedeutet, ist ein Problem in der Erstarrungsstruktur in Abhängigkeit von der chemischen Zusammensetzung der Legierung zu sehen. In der EP 1 469 094 A1 wird beispielsweise vorgeschlagen, einen Schnellstahlumschmelzblock einer Langzeit-Lösungsglühbehandlung zu unterwerfen, wobei eine Abkühlung von 1200°C bis 1300°C auf eine Temperatur von weniger als 900°C mit einer Geschwindigkeit von mehr als 3°C/min erfolgen soll. Derart sind geringe Karbidgrößen mit gleichmäßiger Karbidverteilung im Werkzeugwerkstoff und folglich eine hohe Zähigkeit desselben erreichbar.As previously indicated by a PM production variant, a problem in the solidification structure is seen depending on the chemical composition of the alloy. In the EP 1 469 094 A1 For example, it is proposed to subject a high speed steel remelt block to a long term solution heat treatment wherein cooling should be from 1200 ° C to 1300 ° C to a temperature of less than 900 ° C at a rate greater than 3 ° C / min. Such low carbide sizes with uniform carbide distribution in the tool material and consequently a high toughness of the same can be achieved.

Einen Stahl für spanabhebende Werkzeuge mit niedrigen Kosten für Legierungselemente offenbart die AT 412 285 B . Dieser insbesondere für Kreissägen vorteilhaft verwendbare Stahl nutzt ein bestimmtes Aluminium-zu-Stickstoff-Verhältnis, um den Spanverschleiß am Werkzeug gering zu halten. Allerdings arbeiten Sägezähne bei einer Spanabnahme meist bei geringeren Temperaturen, sodass zumeist keine ausgeprägte Anlasstemperaturbeständigkeit des Werkstoffes gefordert ist.A steel for low cost cutting tools for alloying elements is disclosed AT 412 285 B , This steel, which can be advantageously used in particular for circular saws, uses a specific aluminum-to-nitrogen ratio in order to minimize chip wear on the tool. However, saw teeth usually work at lower temperatures during chip removal, so that in most cases no pronounced tempering temperature resistance of the material is required.

Aus der JP 10 298710 ist eine Stahllegierung bekannt, mit der Zusammensetzung in Gewichtsprozenten C = 0,5-2,3, Si ≤ 3.0, Mn ≤ 1.0, Cr = 3,5-5, Mo ≤ 15, W ≤ 20, V = 0,5-6,0, Al = 0,5 - 3,0. Der Wolframgehalt ist hoch. Hinweise, dass dieser Stahl gute Warm-Umformbarkeit und hohe Zähigkeit bzw. Härtbarkeit besitzt werden nicht gegeben.From the JP 10 298710 is known a steel alloy, with the composition in weight percent C = 0.5-2.3, Si ≤ 3.0, Mn ≤ 1.0, Cr = 3.5-5, Mo ≤ 15, W ≤ 20, V = 0.5- 6.0, Al = 0.5-3.0. The tungsten content is high. Indications that this steel has good hot workability and high toughness or hardenability are not given.

Die Erfindung zielt nun darauf ab, einen Stahl für spanabhebende Werkzeuge zu schaffen, welcher eine feine Erstarrungsstruktur und eine gute Warm-Umformbarkeit aufweist, eine hohe Härteannahme und Anlassbeständigkeit besitzt und hohe Wirtschaftlichkeit bzw. ein günstiges Preis-Leistungsverhältnis zeigt.The invention now aims to provide a steel for cutting tools, which has a fine solidification structure and a good hot workability, has a high hardness acceptance and tempering resistance and shows high efficiency and a favorable price-performance ratio.

Dieses Ziel, welches summarisch erstarrungstechnische, umformtechnische, härtetechnische und wirtschaftliche Probleme löst, wird gemäß der Erfindung erreicht mit einer Stahllegierung für spanabhebende Werkzeuge, im Wesentlichen bestehend aus den Elementen in Gew.-% von:

  • C = 0.76 bis 0.89
  • Si = 0.41 bis 0.59
  • Mn = 0.15 bis 0.39
  • Cr = 3.60 bis 4.60
  • Mo = 2.00 bis 3.15
  • W = 1.50 bis 2.70
  • V = 0.80 bis 1.49
  • Al = 0.60 bis 1.40
  • P = MAX 0.03
  • S = 0.001 bis 0.30
  • N = 0.01 bis 0.10
Fe sowie Verunreinigungselemente als Rest.This object, which solves summarily solidification, forming, curing and economic problems is achieved according to the invention with a steel alloy for cutting tools, consisting essentially of the elements in wt .-% of:
  • C = 0.76 to 0.89
  • Si = 0.41 to 0.59
  • Mn = 0.15 to 0.39
  • Cr = 3.60 to 4.60
  • Mo = 2.00 to 3.15
  • W = 1.50 to 2.70
  • V = 0.80 to 1.49
  • Al = 0.60 to 1.40
  • P = MAX 0.03
  • S = 0.001 to 0.30
  • N = 0.01 to 0.10
Fe and impurity elements as rest.

Die Zusammensetzung der Stahllegierung nach der Erfindung hat metallurgischtechnische Vorteile, die synergetisch auf einen engen Konzentrationsbereich der Legierungselemente beschränkt sind.The composition of the steel alloy according to the invention has metallurgical advantages that are synergistically limited to a narrow concentration range of the alloying elements.

Der Kohlenstoffgehalt bzw. die Kohlenstoffaktivität steht in Wechselwirkung mit dem monokarbidbildenden Element Vanadin, mit den starken Karbidbildnem Molybdän und Wolfram sowie mit Chrom, wobei das Legierungselement Aluminium, welches das Gebiet der kubisch-flächenzentrierten Atomstruktur der Legierung stark einengt, auch, wie sich zeigte, die Erstarrungsstruktur und somit eine Verformbarkeit des Werkstoffes günstig beeinflusst sowie auf ein Härteverhalten und auf eine Anlassbeständigkeit des Werkzeuges hohe Wirkung zeigt.The carbon content or the carbon activity interacts with the monocarbide-forming element vanadium, with the strong carbide-forming molybdenum and Tungsten and chromium, wherein the alloying element aluminum, which strongly restricts the area of the cubic-face-centered atomic structure of the alloy, has also been found to favorably affect the solidification structure and thus deformability of the material, as well as high hardness and toughness resistance of the tool Effect shows.

Im Bereich zwischen 0.60 und 1.40 Gew.-% Aluminium in der Legierung nach der Erfindung wird eine grobe Karbidausscheidung bei einer ledeburitischen Resterstarrung der Schmelze vermindert und eine feinkörnige Karbidbildung im Erstarrungsgefüge erreicht.In the range between 0.60 and 1.40 wt .-% aluminum in the alloy according to the invention, a coarse carbide precipitation in a ledeburitic Resterstarzung the melt is reduced and a fine-grained carbide formation in the solidification microstructure is achieved.

Im Vergleich mit einem Schnellarbeitsstahl-Gussblock der Legierung HS 6-5-2 bzw. DIN Werkstoff Nr. 1.3343 zeigte ein Block mit gleichen Dimensionen jedoch aus einer erfindungsgemäße Legierung eine bessere Verformbarkeit bei höheren Stichabnahmen.In comparison with a high-speed steel cast block of the alloy HS 6-5-2 or DIN material no. 1.3343, however, a block with the same dimensions and made from an alloy according to the invention showed better deformability at higher stitch decreases.

Nach einer Weichglühbehandlung wurde mikroskopisch eine weitgehend gleichmäßige Verteilung der Karbide mit geringer Korngröße im Walzmaterial nach der Erfindung festgestellt.After a soft annealing treatment, a largely uniform distribution of the carbides with a small grain size in the rolled material according to the invention was determined microscopically.

Materialuntersuchungen nach einer thermischen Vergütung mit einer Härtung von einer Temperatur von 1190°C bis 1230°C mit nachfolgender Abkühlung in Öl und einem Anlassen in einem Temperaturbereich von 500°C bis 580°C zeigten folgende Ergebnisse:
Kohlenstoff ab einem Gehalt von 0.76 Gew.-% führt mit einer Konzentration von größer 0.8 Gew.-% Vanadin sowie von größer 1.5 Gew.-% Wolfram und mindestens 2.0 Gew.- % Molybdän in Anwesenheit von mindestens 3.60 Gew.-% Chrom zu einer gewünschten Härteannahme des Werkstückes, wobei Aluminium mit mindestens 0.60 Gew.-% die Durchhärtung fördert, hohe Materialzähigkeit bewirkt und insbesondere die Anlassbeständigkeit zu höheren Temperaturen und längeren Zeiten verschiebt. Höhere Gehalte an Kohlenstoff von 0.89 Gew.-%, an Vanadin von 1.49 Gew.-%, an Wolfram von 2.70 Gew.-% und an Chrom von 4.60 Gew.-% führen auch bei Gehalten von 1.40 Gew.-% Aluminium zu groben Karbidausscheidungen aus der Schmelze und zu nachteilig groben Karbidkörnern im Werkstoff, wobei höhere Aluminiumkonzentrationen als 1.40 Gew.-% auch eine allgemeine Grobkombildung verursachen können. Es wurde auch gefunden, dass bei den Aluminiumgehalten der Stickstoff in Konzentrationsgrenzen von 0.01 bis 0.1 Gew.-% komfeinernd und eigenschaftsverbessernd für das Werkzeug wirkt. Höhere Stickstoffgehalte bilden jedoch zumeist in nachteiliger Weise grobe inhomogen verteilte Nitride im Werkstoff.Material tests after a thermal tempering with a curing of a temperature of 1190 ° C to 1230 ° C with subsequent cooling in oil and a tempering in a temperature range of 500 ° C to 580 ° C showed the following results:
Carbon from a content of 0.76% by weight leads to a concentration of greater than 0.8% by weight of vanadium and also greater than 1.5% by weight of tungsten and at least 2.0% by weight of molybdenum in the presence of at least 3.60% by weight of chromium a desired hardness assumption of the workpiece, wherein aluminum promotes at least 0.60 wt .-% through-curing, high material toughness and in particular shifts the tempering resistance to higher temperatures and longer times. Higher contents of carbon of 0.89% by weight, of vanadium of 1.49% by weight, of tungsten of 2.70% by weight and of chromium of 4.60% by weight lead to coarse even at levels of 1.40% by weight of aluminum Carbide precipitates from the melt and adversely coarse carbide grains in the material, with higher aluminum concentrations than 1.40 wt .-% can also cause a general Grobkombildung. It It has also been found that in the case of aluminum contents, the nitrogen acts in a concentration range of 0.01 to 0.1% by weight and improves the property of the tool for improving the performance of the tool. Higher nitrogen contents, however, usually disadvantageously form coarse inhomogeneously distributed nitrides in the material.

Silizium in den engen Grenzen von 0.41 bis 0.59 Gew,-% im Stahl hat einen vorteilhaften Einfluss auf den Einschlussgehalt und die Härtbarkeit des Werkstoffes, wobei Mangan unterstützend wirkt. Eine Schwefelabbindung zu Mangansulfid kann von einem Teil des Mangangehaltes in der Legierung, welcher Werte von 0.15 bis 0.39 Gew.-% aufweist, sichergestellt werden.Silicon in the narrow limits of 0.41 to 0.59% by weight in steel has a favorable influence on the inclusion content and the hardenability of the material, with manganese acting as a support. Sulfur bonding to manganese sulfide can be ensured from a portion of the manganese content in the alloy which has values of 0.15 to 0.39% by weight.

Bevorzugte Ausführungsformen der Erfindung, die die Eigenschaften der Stahllegierung weiter verbessern können, werden erreicht, wenn diese ein oder mehrere der Elemente in einem engeren Konzentrationsbereich in Gew.-% von:

  • C = 0.80 bis 0.85
  • Si = 0.45 bis 0.55
  • Mn = 0.20 bis 0.30
  • Cr = 4.00 bis 4.39
  • Mo = 2.40 bis 2.80
  • W = 1.90 bis 2.30
  • V = 1.00 bis 1.20
  • Al = 0.80 bis 1.20
aufweist.Preferred embodiments of the invention, which can further improve the properties of the steel alloy, are achieved if these contain one or more of the elements in a narrower concentration range in% by weight of:
  • C = 0.80 to 0.85
  • Si = 0.45 to 0.55
  • Mn = 0.20 to 0.30
  • Cr = 4.00 to 4.39
  • Mo = 2.40 to 2.80
  • W = 1.90 to 2.30
  • V = 1.00 to 1.20
  • Al = 0.80 to 1.20
having.

Es wurde gefunden, dass es günstig für die Materialzähigkeit und vorteilhaft für die Härteannahme des Werkstoffes ist, wenn Molybdän und Wolfram mit Mindestgehalten von 2.00 Gew.-% und 1.50 Gew.-% in der Stahllegierung in einem ausgewogenen Verhältnis enthalten sind. In einer besonders bevorzugten Ausführungsform weist die erfindungsgemäße Legierung eine Konzentration von Molybdän plus der Hälfte der Konzentration von Wolfram einen Wert zwischen 3.3 und 4.0 auf, insbesondere kann mit einem Wert zwischen 3.4 und 3.9 ein überdurchschnittlich günstiges Eigenschaftsprofil des thermisch vergüteten Werkzeuges erreicht werden.It has been found to be favorable for the material toughness and, advantageously, for the hardness acceptance of the material, when molybdenum and tungsten with minimum contents of 2.00% by weight and 1.50% by weight are present in a balanced ratio in the steel alloy. In a particularly preferred embodiment, the alloy according to the invention has a concentration of molybdenum plus half the concentration of tungsten a value between 3.3 and 4.0, in particular can be achieved with a value between 3.4 and 3.9 above average favorable profile of properties of the thermally tempered tool.

Ein spanabhebendes Werkzeug, bestehend aus einer vorzugsweise mindestens 4.1- fach verformten und thermisch vergüteten Stahllegierung mit einer chemischen Zusammensetzung gemäß der Erfindung, besitzt zumindest im Arbeitsbereich eine Materialhärte von größer 63 HRC, hat eine aus angelassenem Martensit gebildete Mikrostruktur, besitzt gute Gebrauchseigenschaften und hohe Zähigkeit im spanabhebenden Betrieb. Die wirtschaftlichen Vorteile der Stahllegierung resultieren aus einer etwa Halbierung der Legierungskosten für Molybdän, Wolfram und Vanadin.A cutting tool, consisting of a preferably at least 4.1 times deformed and thermally tempered steel alloy with a chemical Composition according to the invention, has at least in the working range a material hardness of greater than 63 HRC, has a microstructure formed from tempered martensite, has good performance characteristics and high toughness in the machining operation. The economic advantages of the steel alloy result from an approximately halving of the alloying costs for molybdenum, tungsten and vanadium.

Als ein Ausführungsbeispiel der Erfindung, welches Werkzeuge mit verschiedenen Zusammensetzungen des Stahles im Vergleich mit solchen aus dem Werkstoff HS 6-5-2 bzw. DIN Werkstoff Nr. 1.3343 zeigt, wird im Folgenden näher beschrieben:As an embodiment of the invention, which shows tools with different compositions of the steel in comparison with those of the material HS 6-5-2 or DIN material no. 1.3343, will be described in more detail below:

Drehmesser, die durch Härten und dreimaligen Anlassen thermisch vergütet worden waren, wurde im spanabnehmenden Testbetrieb an einem Werkstück aus dem Werkstoff St33 bzw. aus DIN Werkstoff Nr. 1.0035 im unterbrochenen Schnitt erprobt.Rotary blades, which had been thermally tempered by hardening and tempering three times, were tested in the cutting test mode on a workpiece made of the material St33 or from DIN material no. 1.0035 in an interrupted section.

Die chemische Zusammensetzung und die Härte der Drehmesser sind in der nachfolgenden Tabelle 1 und Tabelle 2 angegeben. Tabelle 1 Werkstoff C Si Mn Cr Mo W V Al N S Mo+W/2 1.HS6-5-2 0.87 0.26 0.25 3.96 4.81 6.68 1.83 - - 0.015 8.15 2.HS6-5-2 0.90 0.21 0.34 4.19 5.20 6.56 1.90 - - 0.009 8.48 Vers.Leg. A 0.80 0.48 0.38 4.51 2.23 2.59 0.92 0.71 0.009 0.02 3.53 Vers.Leg. S 0.83 0.50 0.26 4.20 2.61 2.11 1.11 1.02 0.03 0.064 3.67 Vers.Leg. C 0.88 0.47 0.21 3.74 3.06 1.75 1.38 1.32 0.008 0.005 3.90 Tabelle 2 Werkstoff Härte in HRC 1. HS 6-5-2 64 2. HS 6-5-2 65 Vers.Leg. A 64 Vers.Leg. S 65 Vers.Leg. C 66 The chemical composition and hardness of the rotary knives are given in Table 1 and Table 2 below. Table 1 material C Si Mn Cr Not a word W V al N S Mo + W / 2 1.HS6-5-2 0.87 12:26 12:25 3.96 4.81 6.68 1.83 - - 0015 8.15 2.HS6-5-2 0.90 12:21 12:34 4.19 5.20 6:56 1.90 - - 0009 8:48 Vers.Leg. A 0.80 12:48 12:38 4:51 2.23 2:59 0.92 0.71 0009 12:02 3:53 Vers.Leg. S 0.83 12:50 12:26 4.20 2.61 2.11 1.11 1:02 12:03 0064 3.67 Vers.Leg. C 0.88 12:47 12:21 3.74 3:06 1.75 1:38 1:32 0008 0005 3.90 material Hardness in HRC 1st HS 6-5-2 64 2. HS 6-5-2 65 Vers.Leg. A 64 Vers.Leg. S 65 Vers.Leg. C 66

Bis zum Ausscheiden der Drehmesser im Testbetrieb wegen Verschleiß erfolgten Begutachtungen des Schneidenbereiches, deren Ergebnisse vergleichend in Tabelle 3 angegeben sind, wobei die Werte der Legierung 1 HS 6-5-2 mit jeweils 100% bezeichnet wurde. Tabelle 3 Werkstoff Einsatzzeit % Schneidhaltigkeit % Beständigkeit gegen Kolkverschleiß % 1. HS 6-5-2 30% 100 100 2. HS 6-5-2 30% 105 110 Vers.Leg. A 30% 92 98 Vers.Leg. S 30% 96 100 Vers.Leg. C 30% 94 100 1. HS 6-5-2 60% 100 100 2. HS 6-5-2 60% Bruch der Werkzeugschneide Vers.Leg. A 60% 93 98 Vers.Leg. S 60% 97 100 Vers.Leg. C 60% 95 99 1. HS 6-5-2 90% 100 100 2. HS 6-5-2 90% - - Vers.Leg. A 90% 92 89 Vers.Leg. S 90% 95 92 Vers.Leg. C 90% 92 94 Up to the departure of the rotary knives in the test mode due to wear made assessments of the cutting area, the results are given in Table 3 comparatively, wherein the values of the alloy 1 HS 6-5-2 was designated with 100% each. Table 3 material Mission time% Cutting strength% Resistance to crater wear% 1st HS 6-5-2 30% 100 100 2. HS 6-5-2 30% 105 110 Vers.Leg. A 30% 92 98 Vers.Leg. S 30% 96 100 Vers.Leg. C 30% 94 100 1st HS 6-5-2 60% 100 100 2. HS 6-5-2 60% Breakage of the tool cutting edge Vers.Leg. A 60% 93 98 Vers.Leg. S 60% 97 100 Vers.Leg. C 60% 95 99 1st HS 6-5-2 90% 100 100 2. HS 6-5-2 90% - - Vers.Leg. A 90% 92 89 Vers.Leg. S 90% 95 92 Vers.Leg. C 90% 92 94

An Proben der Versuchslegierung S mit der Bezeichnung S 419 wurden im Vergleich mit 2. HS 6-5-2 Untersuchungen, die Zähigkeit und die Härte in Abhängigkeit der Anlasstemperatur betreffend, durchgeführt.Samples of the experimental alloy S with the designation S 419 were compared with 2. HS 6-5-2 investigations concerning toughness and the hardness depending on the tempering temperature performed.

Fig. 1 zeigt die Zähigkeit (bending strenght) gemessen mit Schlagbiegeproben nach STAHL-EISEN-Prüfblätter (SEP) nach einem Härten von einer Härtetemperatur TH von 1200°C bzw. 1120°C und einem Anlassen im Temperaturbereich zwischen 500°C und 580°C. bzw. 540°C und 580°C. Eine wesentlich höhere Zähigkeit des erfindungsgemäßen Werkstoffes ist auch durch die geringere Karbidmenge von 4 Vol-% (HS 6-5-2 ca. 10 Vol.-%) begründet. Fig. 1 shows the toughness (bending strenght) measured with impact test samples according to STAHL EISEN test sheets (SEP) after hardening from a hardening temperature T H of 1200 ° C or 1120 ° C and tempering in the temperature range between 500 ° C and 580 ° C. or 540 ° C and 580 ° C. A significantly higher toughness of the material according to the invention is also due to the lower amount of carbide of 4% by volume (HS 6-5-2 about 10% by volume).

In Fig. 2 ist die Werkstoffhärte bei einer Härtung von 1200°C bzw. von 1120°C in Abhängigkeit von der Anlasstemperatur wiedergegeben. Bei steigenden Anlasstemperaturen von größer 500°C nähern sich die Härtewerte der Versuchslegierung von unten an jene des 2. HS 6-5-2 an und erreichen bei 580°C das gleiche Niveau von 65 HRC.In Fig. 2 the material hardness is reproduced at a curing of 1200 ° C or 1120 ° C depending on the tempering temperature. With increasing tempering temperatures of greater than 500 ° C, the hardness values of the experimental alloy approach from below to those of the 2nd HS 6-5-2 and reach the same level of 65 HRC at 580 ° C.

Claims (4)

  1. A steel alloy for metal-cutting tools substantially consisting of the following elements in % by weight: C = 0.76 to 0.89 Si = 0.41 to 0.59 Mn = 0.15 to 0.39 Cr = 3.60 to 4.60 Mo = 2.00 to 3.15 W = 1.50 to 2.70 V = 0.80 to 1.49 Al = 0.60 to 1.40 P = MAX 0.03 S = 0.001 to 0.30 N = 0.01 to 0.10
    Fe as well as impurity elements as balance.
  2. The steel alloy according to claim 1 comprising one or more of the elements in a concentration range in % by weight of: C = 0.80 to 0.85 Si = 0.45 to 0.55 Mn = 0.20 to 0.30 Cr = 4.00 to 4.39 Mo = 2.40 to 2.80 W = 1.90 to 2.30 V = 1.00 to 1.20 Al = 0.80 to 1.20
  3. The steel alloy according to claim 1 or 2 wherein the concentration of molybdenum plus half of the concentration of tungsten has a value between 3.3 and 4.0, preferably a value between 3.4 and 3.9.
  4. A metal-cutting tool consisting of a deformed and heat-treated steel alloy according to any one of the claims 1 to 3 with a hardness,present at least in the working area, of more than 63 HRC and a microstructure formed of tempered martensite.
EP07450174.3A 2006-10-27 2007-10-04 Steel alloy for machining tools Not-in-force EP1918401B1 (en)

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AT509598B1 (en) 2010-10-18 2011-10-15 Boehler Edelstahl Gmbh & Co Kg METHOD FOR PRODUCING TOOLS FROM ALLOYED STEEL AND TOOLS, IN PARTICULAR FOR DISPERSING MACHINING METALS
EP2662462A1 (en) * 2012-05-07 2013-11-13 Valls Besitz GmbH Low temperature hardenable steels with excellent machinability

Family Cites Families (18)

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GB756738A (en) * 1952-05-29 1956-09-05 Steirische Gussstahlwerke Improvements in or relating to high-speed steel
JPH0765141B2 (en) * 1985-09-18 1995-07-12 日立金属株式会社 Tool steel for hot working
JPS63118054A (en) * 1986-11-06 1988-05-23 Sumitomo Metal Ind Ltd High-speed tool steel having superior toughness
JP2564534B2 (en) * 1987-02-27 1996-12-18 日立金属株式会社 High speed tool steel
JPH01111846A (en) * 1987-10-27 1989-04-28 Daido Steel Co Ltd Hot-working tool
JPH02285050A (en) * 1989-04-26 1990-11-22 Nippon Steel Corp High hardness free-cutting die steel
EP0599910B1 (en) * 1991-08-07 1997-03-05 Erasteel Kloster Aktiebolag High-speel manufactured by powder metallurgy
RU2103410C1 (en) * 1992-11-05 1998-01-27 Кремнев Леонид Стефанович Instrumental steel
JP3414855B2 (en) * 1994-08-02 2003-06-09 大同特殊鋼株式会社 High speed tool steel for precision casting
JPH10298710A (en) * 1997-04-28 1998-11-10 Daido Steel Co Ltd Tool steel for surface modification
JPH10330894A (en) * 1997-06-05 1998-12-15 Daido Steel Co Ltd Low alloy high speed tool steel and its production
CN1092243C (en) * 1999-01-26 2002-10-09 尹道乐 Economic high speed steel
JP2001150122A (en) * 1999-11-25 2001-06-05 Hitachi Metals Ltd Manufacturing method of stock for cold/warm plastic working and its cold/warm plastic working method
JP2001200341A (en) * 2000-01-20 2001-07-24 Sanyo Special Steel Co Ltd Tool steel excellent in earth and sand wear property
KR20050007597A (en) * 2002-06-13 2005-01-19 우데홀름툴링악티에보라그 Cold work steel and cold work tool
JP2004285444A (en) * 2003-03-24 2004-10-14 Daido Steel Co Ltd Low-alloy high-speed tool steel showing stable toughness
JP4179024B2 (en) 2003-04-09 2008-11-12 日立金属株式会社 High speed tool steel and manufacturing method thereof
AT412285B (en) 2003-06-23 2004-12-27 Boehler Bleche Gmbh STEEL FOR DISCONTINUING TOOLS

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AT504331B1 (en) 2008-05-15
AR063489A1 (en) 2009-01-28
EP1918401A3 (en) 2012-05-30
US20080101980A1 (en) 2008-05-01
ES2430201T3 (en) 2013-11-19
BRPI0703665A (en) 2008-06-10
AT504331B8 (en) 2008-09-15
JP5046111B2 (en) 2012-10-10
CA2607641A1 (en) 2008-04-27
CA2607641C (en) 2012-08-21
AU2007229405B2 (en) 2009-03-26
BRPI0703665B1 (en) 2014-02-18
AU2007229405A1 (en) 2008-05-15
AT504331A4 (en) 2008-05-15
SI1918401T1 (en) 2013-12-31
US7655101B2 (en) 2010-02-02
JP2008111194A (en) 2008-05-15

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