EP1693138B1 - Cutting tool - Google Patents

Cutting tool Download PDF

Info

Publication number
EP1693138B1
EP1693138B1 EP06450021A EP06450021A EP1693138B1 EP 1693138 B1 EP1693138 B1 EP 1693138B1 EP 06450021 A EP06450021 A EP 06450021A EP 06450021 A EP06450021 A EP 06450021A EP 1693138 B1 EP1693138 B1 EP 1693138B1
Authority
EP
European Patent Office
Prior art keywords
cutting tool
content
well
less
tool according
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP06450021A
Other languages
German (de)
French (fr)
Other versions
EP1693138A1 (en
Inventor
Ziya Devrim Dr. Caliskanoglu
Ingrid Schemmel
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Voestalpine Boehler Edelstahl GmbH
Original Assignee
Boehler Edelstahl GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Boehler Edelstahl GmbH filed Critical Boehler Edelstahl GmbH
Priority to PL06450021T priority Critical patent/PL1693138T3/en
Priority to SI200630007T priority patent/SI1693138T1/en
Publication of EP1693138A1 publication Critical patent/EP1693138A1/en
Application granted granted Critical
Publication of EP1693138B1 publication Critical patent/EP1693138B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a cutting tool, in particular a knife for a wood chip.
  • Knives made of this steel have a high material toughness in the thermally tempered state, but their wear resistance, the dimensional stability of the cutting area and the corrosion resistance are usually too low.
  • knives or blade strips are often made of steel according to material no. 1.2363 manufactured, which cutting tools usually have no sufficient wear resistance. It has already been tried, as a cutting tool material according to an alloy AT 393 387 B respectively.
  • EP 0425471 A1 with the best results in terms of wear behavior, but occasionally errors occurred which pointed to too low material toughness.
  • the invention has the object to overcome the respective disadvantages of the prior art and to provide a cutting tool, in particular a knife, of the type mentioned, which due to a narrow selection of the concentration of the respective elements in the steel or the chemical composition and the thermal compensation and the microstructure of the material synergistically improved performance characteristics in a machining, in particular a chip, wood with intermittent load or interrupted cut.
  • a high toughness of the tool material has been found to be required because at a stroke value measured on a percussion test in the longitudinal direction of less than 100J, breakouts at the cutting edges and even knife breaks may occur.
  • high material hardness values which ensure a high dimensional stability of the entire cutting area at high impact loads are necessary.
  • a hardness of less than 60 HRC allows plastic deformation of the tool material, which can lead to a deterioration of the tool function in the cutting operation.
  • the concentration of the respective alloying elements is important in accordance with the invention because they determine the precipitation and transformation kinetics and the microstructure in the case of a thermal treatment.
  • the content of carbon is to be considered simultaneously with the content or the activity of the respective carbide-forming elements in relation to carbon.
  • carbon produced by 0.5 to 0.7 wt .-% vanadium monocarbides, which have a small diameter, and are homogeneously distributed and thus with a content of at least 0.35 vol .-% make a significant contribution to the wear resistance of the material without negatively affecting its toughness.
  • Higher levels of carbon and vanadium may be detrimental to the interaction of the alloying elements and tend to result in coarser carbide structure, thereby degrading material toughness.
  • Low concentrations of these elements of less than 0.7% by weight Carbon and 0.5 wt .-% vanadium reduce disproportionately the wear resistance of the material.
  • the carbon content of the alloy is also defined with respect to a shaping of M 7 C 3 and M 23 C 6 carbides with the other carbide-forming elements of the steel in the range of 0.7 to 0.9 wt .-%, with what content the desired properties of the matrix consisting of tempered martensite can be achieved.
  • the respective concentration of chromium and molybdenum in the range of 7.5 to 8.5 or 1.4 to 1.8 are essential for a desired total carbide content of greater than 3.0 vol .-%, however, is a material embrittling effect because of Tungsten content limited to a value of less than 0.3 wt .-%.
  • Manganese at levels of 0.35 to 0.45, promotes hardenability of the steel and binds the sulfur, which is believed to have a concentration level below 0.005 weight percent, to manganese sulfide.
  • Nickel has a disruptive effect on the precipitation and conversion kinetics of this cutting steel in a tempering treatment, so that a Ni content of less than 0.4% by weight is essential for the desired quality of the tool.
  • the inventively provided content of aluminum in the steel within the limits of 0.003 to 1.0 wt .-% on the one hand has a particularly favorable effect on the hardness and tempering behavior or on the remuneration structure and the mechanical properties of the material, on the other hand by aluminum as well the quality of a surface layer, such as a nitride layer, or the adhesion of a coating, such as a deposited after the PVD or CVD nitride, carbonitride or oxide carbonitride layer of metals, in particular of titanium and / or chromium promoted.
  • Aluminum increases the activity and the diffusion coefficient of carbon in austenite.
  • the diffusion coefficients of chromium, molybdenum and vanadium are reduced by aluminum in the austenite and in the ferrite. This means a reduction in the solubility of carbon in the austenite, so that the stability of the austenite is lowered and therefore the martensite starting point is increased, which in turn reduces the residual austenite content in the austenite hardened structure is greatly lowered.
  • Aluminum is mainly dissolved in the matrix and contributes to the solid solution hardness. The high affinity of aluminum for nitrogen increases the hardness of the diffusion layer of nitrided steels.
  • An aluminum content of 0.15 to 0.25 wt .-% in the alloy is preferred.
  • a "chipper knife” made according to the invention parallel to the testing tool, was used in a device for cutting logs in difficult conditions by adhering earth particles and provided the market in comparison with a high-performance knife arranged next to it Service life improvement of 120%.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Heat Treatment Of Articles (AREA)
  • Auxiliary Devices For Machine Tools (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Cutting tool comprises an iron alloy containing (wt.%): carbon (0.7-0.9), silicon (less than 0.8), manganese (0.35-0.45), sulfur (less than 0.005), chromium (7.5-8.5), molybdenum (1.4-1.8), nickel (less than 0.4), vanadium (0.5-0.7), tungsten (less than 0.3) and aluminum (0.003-1.0). The heat-treated alloy has a total carbide content of more than 3 vol.%, of which at least 0.35 vol.% is monocarbide, and the matrix consists of martensite.

Description

Die Erfindung bezieht sich auf ein Schneidwerkzeug, insbesondere ein Messer für eine Spanung von Holz.The invention relates to a cutting tool, in particular a knife for a wood chip.

In der holzverarbeitenden Industrie sind für eine Spanung von Holz, insbesondere von Stammholz, also für sogenannte "Chipper-Anwendungen", Messer oder Messerleisten eingesetzt, die gleichzeitig auf Verschleiß durch adhäsive und abrasive Belastung, auf Biegung und auf Druck im Schneidkantenbereich vornehmlich schlagartig beansprucht werden. Der Werkstoff derartiger Werkzeuge bzw. Messer soll demnach in korrosionschemischer Hinsicht auch der Belastung durch Tannin wegen beständig sein und mittels einer thermischen Vergütebehandlung gleichzeitig höchste Zähigkeit und höchste Verschleißfestigkeit sowie eine hohe Härte erhalten bzw. aufweisen.In the woodworking industry are for wood, in particular of logs, so for so-called "chipper applications", knife or knife strips used, which are claimed at the same time primarily for wear due to adhesive and abrasive stress, bending and pressure in the cutting edge area , Accordingly, the material of such tools or knives should also be resistant to stress from tannin in terms of corrosion chemistry and at the same time obtain and / or have the highest toughness and highest wear resistance and high hardness by means of thermal tempering treatment.

Die Forderungen nach stetig steigender Leistung bei höchster Betriebssicherheit der Holzverarbeitungsanlagen können letzlich nur durch Schneidwerkzeuge mit entsprechend abgestimmtem Eigenschaftsprofil erfüllt werden. Mit anderen Worten: Insbesondere im Schneidenbereich der Messer sind ein Verschleiß, Kantenschäden durch einerseits plastische Verformungen, andererseits durch muschelige oder linsenförmige Ausbrüche der Kanten hauptsächlich infolge von Stoßbelastungen sowie ein vorzeitiger Messerbruch durch aufeinander abgestimmte Materialeigenschaften hintanzuhalten.The demands for steadily increasing performance with maximum operational reliability of the wood processing plants can ultimately only be met by cutting tools with a correspondingly matched property profile. In other words: Especially in the cutting area of the knife wear, edge damage by plastic deformation on the one hand, on the other hand by mussel or lenticular outbreaks of edges mainly due to shock loads and a premature knife break due to matched material properties are to be held.

Für "Chipper-Anwendungen" ist es bekannt, Stähle mit der Werkstoff-Nr. 1.2362 nach DIN einzusetzen. Messer aus diesem Stahl besitzen im thermisch vergüteten Zustand eine hohe Materialzähigkeit, jedoch ist deren Verschleißfestigkeit, die Formstabilität des Schneidenbereiches und die Korrosionsbeständigkeit meist zu gering. Zur Verbesserung der Formstabilität der Schneide werden Messer bzw. Messerleisten vielfach aus Stahl gemäß Werkstoff-Nr. 1.2363 gefertigt, welche Schneidwerkzeuge zumeist keine ausreichende Verschleißfestigkeit aufweisen. Es wurde schon versucht, als Schneidwerkzeug-Werkstoff eine Legierung gemäß AT 393 387 B bzw. EP 0425 471 A1 zu verwenden, wobei hinsichtlich des Verschleißverhaltens beste Ergebnisse erreicht werden konnten, allerdings kam es gelegentlich zu Fehlern, die auf zu geringe Materialzähigkeit hinwiesen.For "Chipper applications" it is known steels with the material no. 1.2362 according to DIN. Knives made of this steel have a high material toughness in the thermally tempered state, but their wear resistance, the dimensional stability of the cutting area and the corrosion resistance are usually too low. In order to improve the dimensional stability of the blade, knives or blade strips are often made of steel according to material no. 1.2363 manufactured, which cutting tools usually have no sufficient wear resistance. It has already been tried, as a cutting tool material according to an alloy AT 393 387 B respectively. EP 0425471 A1 with the best results in terms of wear behavior, but occasionally errors occurred which pointed to too low material toughness.

Die Erfindung setzt sich zum Ziel, die jeweiligen Nachteile im Stand der Technik zu überwinden und ein Schneidwerkzeug, insbesondere ein Messer, der eingangs genannten Art zu schaffen, welches aufgrund einer engen Auswahl der Konzentration der jeweiligen Elemente im Stahl bzw. der chemischen Zusammensetzung sowie der thermischen Vergütung und der Mikrostruktur des Werkstoffes synergetisch verbesserte Gebrauchseigenschaften bei einer Bearbeitung, insbesondere einer Spanung, von Holz mit stoßweiser Belastung oder unterbrochenem Schnitt aufweist.The invention has the object to overcome the respective disadvantages of the prior art and to provide a cutting tool, in particular a knife, of the type mentioned, which due to a narrow selection of the concentration of the respective elements in the steel or the chemical composition and the thermal compensation and the microstructure of the material synergistically improved performance characteristics in a machining, in particular a chip, wood with intermittent load or interrupted cut.

Dieses Ziel wird erreicht mit einem Schneidwerkzeug gemäß Anspruch 1.This object is achieved with a cutting tool according to claim 1.

Die mit der Erfindung erreichten Vorteile sind im Wesentlichen darin zu sehen, dass durch die enge Auswahl der jeweiligen Gehalte der Legierungselemente in einer Abstimmung aufeinander und einer gebräuchlichen thermischen Vergütung des Stahles mit einem Härten mit einem Abkühlen von etwa 1030°C gefolgt von einem dreimaligen Anlassen bei einer Temperatur von etwa 550°C und einem Schaffen einer erwünschten Mikrostruktur die geforderten bzw. die gewünschten Einzeleigenschaften gleichzeitig maximiert werden.The advantages achieved with the invention are essentially to be seen therein that by closely selecting the respective contents of the alloying elements in coordination with one another and a conventional thermal tempering of the steel with a hardening with a cooling of about 1030 ° C followed by a three times tempering at a temperature of about 550 ° C and a desired Microstructure the required or the desired individual properties are maximized simultaneously.

Eine hohe Zähigkeit des Werkzeugwerkstoffes ist, wie gefunden wurde, erforderlich, weil bei einem Wert für die Schlagarbeit gemessen an einer Schlagbiegeprobe in Längsrichtung von weniger als 100J Ausbrüche an den Schneidkanten und sogar Messerbrüche entstehen können. Gleichzeitig sind erfindungsgemäß hohe Materialhärtewerte, welche eine weitgehende Formstabilität des gesamten Schneidenbereiches bei hohen schlagartigen Belastungen sicherstellen, notwendig. Eine Härte von weniger als 60 HRC ermöglicht plastische Verformungen des Werkzeugmaterials, was zu einer Beeinträchtigung der Werkzeugfunktion im spanenden Betrieb führen kann.A high toughness of the tool material has been found to be required because at a stroke value measured on a percussion test in the longitudinal direction of less than 100J, breakouts at the cutting edges and even knife breaks may occur. At the same time, according to the invention, high material hardness values which ensure a high dimensional stability of the entire cutting area at high impact loads are necessary. A hardness of less than 60 HRC allows plastic deformation of the tool material, which can lead to a deterioration of the tool function in the cutting operation.

Für eine chemische Beständigkeit und für das Profil der mechanischen Eigenschaften des Werkzeugwerkstoffes ist die Konzentration der jeweiligen Legierungselemente erfindungsgemäß wichtig, weil diese die Ausscheidungs- und Umwandlungskinetik und die Gefügestruktur bei einer thermischen Vergütung bestimmen.For chemical resistance and for the profile of the mechanical properties of the tool material, the concentration of the respective alloying elements is important in accordance with the invention because they determine the precipitation and transformation kinetics and the microstructure in the case of a thermal treatment.

Bei einer Relation der Legierungselemente ist insbesondere der Gehalt an Kohlenstoff gleichzeitig mit dem Gehalt bzw. der Aktivität der jeweiligen karbidbildenden Elemente zu Kohlenstoff zu sehen. In einem engen Bereich von 0,7 bis 0,9 Gew.-% Kohlenstoff entstehen durch 0,5 bis 0,7 Gew.-% Vanadin Monokarbide, die einen geringen Durchmesser aufweisen, sowie homogen verteilt sind und derart mit einem Gehalt von mindestens 0,35 Vol.-% einen wesentlichen Beitrag zur Verschleißbeständigkeit des Werkstoffes liefern, ohne dessen Zähigkeit negativ zu beeinflussen. Höhere Gehalte an Kohlenstoff und Vanadin können sich auf die Wechselwirkung der Legierungselemente nachteilig auswirken und führen zumeist zu gröberer Karbidstruktur, wodurch die Materialzähigkeit verschlechtert wird. Niedrige Konzentrationen dieser Elemente von weniger als 0,7 Gew.-% Kohlenstoff und 0,5 Gew.-% Vanadin mindern überproportional die Verschleißfestigkeit des Werkstoffes.In the case of a relation of the alloying elements, in particular the content of carbon is to be considered simultaneously with the content or the activity of the respective carbide-forming elements in relation to carbon. In a narrow range of 0.7 to 0.9 wt .-% carbon produced by 0.5 to 0.7 wt .-% vanadium monocarbides, which have a small diameter, and are homogeneously distributed and thus with a content of at least 0.35 vol .-% make a significant contribution to the wear resistance of the material without negatively affecting its toughness. Higher levels of carbon and vanadium may be detrimental to the interaction of the alloying elements and tend to result in coarser carbide structure, thereby degrading material toughness. Low concentrations of these elements of less than 0.7% by weight Carbon and 0.5 wt .-% vanadium reduce disproportionately the wear resistance of the material.

Der Kohlenstoffgehalt der Legierung ist auch im Hinblick auf eine Ausformung von M7C3 und M23C6 Karbiden mit den weiteren karbidbildenden Elementen des Stahles erfindungsgemäß im Bereich von 0,7 bis 0,9 Gew.-% festgelegt, mit welchem Gehalt auch die gewünschten Eigenschaften der Matrix, die aus angelassenem Martensit besteht, erreicht werden. Dabei sind die jeweilige Konzentration von Chrom und Molybdän im Bereich von 7,5 bis 8,5 bzw. 1,4 bis 1,8 wesentlich für einen gewünschten Gesamtkarbidgehalt von größer 3,0 Vol.-%, hingegen ist einer materialversprödenden Wirkung wegen der Wolframgehalt auf einen Wert von kleiner 0,3 Gew.-% eingeschränkt.The carbon content of the alloy is also defined with respect to a shaping of M 7 C 3 and M 23 C 6 carbides with the other carbide-forming elements of the steel in the range of 0.7 to 0.9 wt .-%, with what content the desired properties of the matrix consisting of tempered martensite can be achieved. The respective concentration of chromium and molybdenum in the range of 7.5 to 8.5 or 1.4 to 1.8 are essential for a desired total carbide content of greater than 3.0 vol .-%, however, is a material embrittling effect because of Tungsten content limited to a value of less than 0.3 wt .-%.

Mangan fördert in Gehalten von 0,35 bis 0,45 die Härtbarkeit des Stahles und bindet den Schwefel, der einen Konzentrationswert von unter 0,005 Gew.-% aufweisen soll, zu Mangansulfid.Manganese, at levels of 0.35 to 0.45, promotes hardenability of the steel and binds the sulfur, which is believed to have a concentration level below 0.005 weight percent, to manganese sulfide.

Nickel wirkt störend auf die Ausscheidungs- und Umwandlungskinetik dieses Schneidstahles bei einer Vergütungsbehandlung, sodass ein Ni-Gehalt von unter 0,4 Gew.-% wesentlich für die gewünschte Werkzeuggüte ist.Nickel has a disruptive effect on the precipitation and conversion kinetics of this cutting steel in a tempering treatment, so that a Ni content of less than 0.4% by weight is essential for the desired quality of the tool.

Der erfindungsgemäß vorgesehene Gehalt von Aluminium im Stahl in den Grenzen von 0,003 bis 1,0 Gew.-% wirkt sich einerseits besonders günstig auf das Härte-und Anlassverhalten bzw. auf das Vergütungsgefüge und die mechanischen Eigenschaften des Werkstoffes aus, andererseits wird durch Aluminium auch die Güte einer Oberflächenschicht, beispielsweise einer Nitridschicht, oder die Haftung einer Beschichtung, beispielsweise einer nach dem PVD oder CVD aufgebrachten Nitrid-, Karbonitrid- oder Oxidkarbonitrid-Schicht von Metallen, insbesondere von Titan und/oder Chrom, gefördert. Aluminium erhöht die Aktivität und den Diffusionskoeffizienten von Kohlenstoff im Austenit. Die Diffusionskoeffizienten von Chrom, Molybdän und Vanadin werden durch Aluminium im Austenit und im Ferrit gesenkt. Das bedeutet eine Verringerung der Löslichkeit von Kohlenstoff im Austenit, sodass die Stabilität des Austenits gesenkt und daher der Martensitstartpunkt erhöht wird, wodurch wiederum der Restaustenitgehalt im gehärteten Gefüge stark abgesenkt wird. Aluminium wird hauptsächlich in der Matrix gelöst und liefert einen Beitrag zur Mischkristallhärte. Die hohe Affinität von Aluminium zu Stickstoff erhöht die Härte der Diffusionsschicht von nitrierten Stählen.The inventively provided content of aluminum in the steel within the limits of 0.003 to 1.0 wt .-% on the one hand has a particularly favorable effect on the hardness and tempering behavior or on the remuneration structure and the mechanical properties of the material, on the other hand by aluminum as well the quality of a surface layer, such as a nitride layer, or the adhesion of a coating, such as a deposited after the PVD or CVD nitride, carbonitride or oxide carbonitride layer of metals, in particular of titanium and / or chromium promoted. Aluminum increases the activity and the diffusion coefficient of carbon in austenite. The diffusion coefficients of chromium, molybdenum and vanadium are reduced by aluminum in the austenite and in the ferrite. This means a reduction in the solubility of carbon in the austenite, so that the stability of the austenite is lowered and therefore the martensite starting point is increased, which in turn reduces the residual austenite content in the austenite hardened structure is greatly lowered. Aluminum is mainly dissolved in the matrix and contributes to the solid solution hardness. The high affinity of aluminum for nitrogen increases the hardness of the diffusion layer of nitrided steels.

Bevorzugt ist ein Aluminiumgehalt von 0,15 bis 0,25 Gew.-% in der Legierung.An aluminum content of 0.15 to 0.25 wt .-% in the alloy is preferred.

Anhand eines Beispieles soll die Erfindung näher dargelegt werden:
Eine Schmelze mit einer Zusammensetzung von in Gew.-% C = 0,81, Si = 0,68, Mn = 0,39, P = 0,015, S = 0,003, Cr = 8,06, Mo = 1,59, Ni = 0,26, V = 0,61, W = 0,19, Al = 0,17, Fe Rest wurde nach einer pfannenmetallurgischen Behandlung zu Blöcken gegossen. Nach einer Rückwärm- und Glühzeit von 31 Stunden erfolgte eine Walzung zu Flachmaterial, aus welchem durch mechanische Bearbeitung eine Fertigung von "Chipper-Messern" erfolgte.By way of example, the invention will be explained in more detail:
A melt having a composition of wt% C = 0.81, Si = 0.68, Mn = 0.39, P = 0.015, S = 0.003, Cr = 8.06, Mo = 1.59, Ni = 0.26, V = 0.61, W = 0.19, Al = 0.17, Fe remainder was cast into blocks after a ladle metallurgical treatment. After a heat-back and annealing time of 31 hours, a rolling to flat material, from which by machining a production of "Chipper knives" was carried out.

Nach einem Auf- und Durchwärmen der Messer bzw. der Messerleisten auf 1030°C erfolgte eine forcierte Abkühlung derselben auf eine Temperatur von ca. 50°C, der ein dreimaliges Anlassen bei einer Temperatur zwischen 545°C und 560°C nachgeordnet wurde. Nach diesem thermischen Vergüten betrug die Härte des Werkstoffes aus einem Erprobungswerkzeug 61 HRC frei von Restaustenit. Aus gegenständlichem Werkzeug erfolgte eine Entnahme von Schlagbiegeproben mit den Abmessungen: Länge 55 mm, Breite 10 mm und Höhe 7 mm. Eine Zähigkeitsuntersuchung des Werkstoffes mit diesen Proben erbrachte eine Schlagbiegearbeit von im Wesentlichen 115J. Metallographische und Rückstanduntersuchungen zeigten, dass der Werkstoff in einer Matrix aus angelassenem Martensit eine Gesamtmenge an Karbiden von 3,21 Vol.-% aufwies, von welchen Karbiden 0,43 Vol.-% Monokarbide vom Typ MC und der Rest Karbide der Formation M7C3 und M23C6 waren. Dabei ist festzuhalten, dass keinerlei Restaustenti im Gefüge vorlag.After heating up and warming the knife or the knife strips to 1030 ° C forced cooling took place to a temperature of about 50 ° C, which was followed by a three times tempering at a temperature between 545 ° C and 560 ° C. After this thermal quenching, the hardness of the material from a testing tool 61 HRC was free of retained austenite. From objective tool a removal of impact samples with the dimensions took place: length 55 mm, width 10 mm and height 7 mm. Toughness testing of the material with these samples resulted in impact bending work of essentially 115J. Metallographic and residue investigations showed that the material in a martensite tempered matrix had a total of 3.21% by volume carbides, of which carbides were 0.43% by volume MC type monocarbons and the remainder M 7 carbides C 3 and M 23 were C 6 . It should be noted that there was no Restaustenti in the structure.

Eine parallel zum Erprobungswerkzeug gefertigtes, erfindungsgemäßes "Chipper-Messer" wurde in einer Einrichtung zum Spanen von Stammholz bei erschwerten Bedingungen durch anhaftende Erdpartikel eingesetzt und erbrachte im Vergleich mit einem daneben angeordneten Hochleistungsmesser vom Markt eine Standzeitverbesserung von 120%.A "chipper knife" made according to the invention, parallel to the testing tool, was used in a device for cutting logs in difficult conditions by adhering earth particles and provided the market in comparison with a high-performance knife arranged next to it Service life improvement of 120%.

Claims (4)

  1. A cutting tool, in particular a knive for machining wood as well as for products with wood, such as chipboards and the like, having a material toughness of more than 100J measured in longitudinal direction as impact energy AV (SBP) pursuant to Stahl-Eisen-Prüfblatt [Steel/Iron Test Sheet] (SEP) 1314, with a material hardness of more than 60 HRC and increased corrosion resistance as well as wear resistance thereof consisting of an alloy with a chemical composition in % by weight of: C = 0.7 to 0.9 Si = ≤ 0.8 Mn = 0.35 to 0.45 S = < 0.005 Cr = 7.5 to 8.5 Mo = 1.4 to 1.8 Ni = < 0.4 V = 0.5 to 0.7 W = < 0.3 Al = 0.003 to 1.0 Fe = remainder as well as production-related contaminations,
    wherein the thermally treated material of the cutting tool has a total carbide content of more than 3 % by volume, of which at least 0.35 % by volume are monocarbides and the matrix consists of annealed martensite.
  2. The cutting tool according to Claim 1, wherein the alloy has an Al content of 0.15 to 0.25 % by weight.
  3. The cutting tool according to Claim 1 or 2, which has a coating which is preferably formed as a compound with carbon and/or nitrogen and/or oxygen.
  4. The cutting tool according to Claim 3, in which the coating contains a chromium compound.
EP06450021A 2005-02-21 2006-02-15 Cutting tool Active EP1693138B1 (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL06450021T PL1693138T3 (en) 2005-02-21 2006-02-15 Cutting tool
SI200630007T SI1693138T1 (en) 2005-02-21 2006-02-15 Cutting tool

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
AT0028605A AT500728B8 (en) 2005-02-21 2005-02-21 CUTTING TOOL

Publications (2)

Publication Number Publication Date
EP1693138A1 EP1693138A1 (en) 2006-08-23
EP1693138B1 true EP1693138B1 (en) 2007-08-29

Family

ID=36037228

Family Applications (1)

Application Number Title Priority Date Filing Date
EP06450021A Active EP1693138B1 (en) 2005-02-21 2006-02-15 Cutting tool

Country Status (8)

Country Link
EP (1) EP1693138B1 (en)
AT (2) AT500728B8 (en)
BR (1) BRPI0600508B1 (en)
CA (1) CA2537018C (en)
DE (1) DE502006000071D1 (en)
ES (1) ES2292161T3 (en)
PL (1) PL1693138T3 (en)
SI (1) SI1693138T1 (en)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2008066438A1 (en) * 2006-11-27 2008-06-05 E2 Forestry Hb Wear resistant tool for wood chipping

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS53130217A (en) * 1977-04-20 1978-11-14 Hitachi Metals Ltd Precipitation hardening type abrasionn resistant steel for nitriding use
US4353743A (en) * 1979-05-29 1982-10-12 Bethlehem Steel Corporation Steel composition for chipper knife
US4353756A (en) * 1979-05-29 1982-10-12 Bethlehem Steel Corporation Method of heat treating a steel composition for chipper knife
US4287007A (en) * 1979-05-29 1981-09-01 Bethlehem Steel Corporation Steel composition chipper knife
AT372709B (en) * 1979-12-20 1983-11-10 Ver Edelstahlwerke Ag ALLOY STEEL CUTTING TOOL
FI854000L (en) * 1985-10-25 1987-04-16 Vsesojuzny Nauchno-Issledovatelsky Instrumentalny Institut SCREENING WITH A SLIDING SYSTEM.
AT393387B (en) * 1989-10-23 1991-10-10 Boehler Gmbh COLD WORK STEEL WITH HIGH PRESSURE STRENGTH AND USE OF THIS STEEL
JP3461041B2 (en) * 1994-09-13 2003-10-27 日立金属株式会社 Knife for shearing steel plate
SE518958C2 (en) * 2001-04-25 2002-12-10 Uddeholm Tooling Ab Steel article used as mold tools, consists of alloy of preset elements and has micro-structure containing carbides of specific type, obtained by spray forming ingot
AT412285B (en) * 2003-06-23 2004-12-27 Boehler Bleche Gmbh STEEL FOR DISCONTINUING TOOLS

Also Published As

Publication number Publication date
CA2537018A1 (en) 2006-08-21
BRPI0600508A (en) 2006-11-07
BRPI0600508B1 (en) 2015-09-22
DE502006000071D1 (en) 2007-10-11
EP1693138A1 (en) 2006-08-23
ATE371513T1 (en) 2007-09-15
PL1693138T3 (en) 2008-01-31
SI1693138T1 (en) 2007-12-31
AT500728A4 (en) 2006-03-15
AT500728B1 (en) 2006-03-15
AT500728B8 (en) 2007-02-15
ES2292161T3 (en) 2008-03-01
CA2537018C (en) 2010-08-03

Similar Documents

Publication Publication Date Title
EP0319511B1 (en) Bimetallic strip for metal saw blades
AT393387B (en) COLD WORK STEEL WITH HIGH PRESSURE STRENGTH AND USE OF THIS STEEL
EP1249511B1 (en) High speed steel with good high temperature strength manufactured by powder metallurgy
EP1300482B1 (en) Hot-work tool-steel article
EP3323902A1 (en) Steel material containing hard particles prepared by powder metallurgy, method for producing a component from such a steel material and component produced from the steel material
DE2800444C2 (en) Use of a Cr-Mo steel
EP0751234B1 (en) Blade body for saws such as circular or gang saws, cutting discs and cutting or scrapping apparatus
EP2223763B1 (en) Bimetallic saw
EP1693138B1 (en) Cutting tool
AT398176B (en) BI-METAL BAND ROLLING AND BI-METAL SAW BLADE MADE OF IT
EP3323903B1 (en) Steel material prepared by powder metallurgy, method for producing a component from such a steel material and component produced from the steel material
DE202010018445U1 (en) Scissors knife of a scrap shear
EP0566560B1 (en) Material for the cutting edge of bi-metal saw blades
EP1918401B1 (en) Steel alloy for machining tools
EP1471160B1 (en) Cold-worked Steel Object
AT401387B (en) CORROSION RESISTANT ALLOY AND METHOD FOR PRODUCING CORROSION RESISTANT CUTTERS
EP1493833B1 (en) Steel for machine cutting tools
EP1382704B1 (en) Cold work steel with high wear resistance
JPH06212365A (en) Steel for band saw and its production
EP2233596B1 (en) Cold worked steel object
EP1358359B1 (en) Steel and method for producing an intermediate product
DE29510690U1 (en) Base material for the production of master blades for circular saws, cutting discs, frame saws as well as cutting and scraping devices

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

AX Request for extension of the european patent

Extension state: AL BA HR MK YU

17P Request for examination filed

Effective date: 20060906

17Q First examination report despatched

Effective date: 20061122

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

AKX Designation fees paid

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REF Corresponds to:

Ref document number: 502006000071

Country of ref document: DE

Date of ref document: 20071011

Kind code of ref document: P

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: HEPP, WENGER & RYFFEL AG

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

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

Effective date: 20071128

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

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20071229

REG Reference to a national code

Ref country code: PL

Ref legal event code: T3

ET Fr: translation filed
REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2292161

Country of ref document: ES

Kind code of ref document: T3

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

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

REG Reference to a national code

Ref country code: IE

Ref legal event code: FD4D

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

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20071130

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

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

Ref country code: IE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20080129

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

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

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20080530

BERE Be: lapsed

Owner name: BOHLER EDELSTAHL GMBH

Effective date: 20080228

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

Ref country code: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20080228

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

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

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

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20080228

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

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20080215

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

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

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

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20071129

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

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20080301

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20080215

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

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20070829

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006000071

Country of ref document: DE

Representative=s name: HGF EUROPE LLP, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006000071

Country of ref document: DE

Representative=s name: HGF EUROPE LP, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006000071

Country of ref document: DE

Representative=s name: PATRONUS IP PATENT UND RECHTSANWAELTE, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006000071

Country of ref document: DE

Representative=s name: PATRONUS IP PATENT- UND RECHTSANWAELTE, DE

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 12

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 13

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006000071

Country of ref document: DE

Representative=s name: HGF EUROPE LLP, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502006000071

Country of ref document: DE

Representative=s name: HGF EUROPE LP, DE

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

Ref country code: NL

Payment date: 20230226

Year of fee payment: 18

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

Ref country code: FR

Payment date: 20230223

Year of fee payment: 18

Ref country code: FI

Payment date: 20230223

Year of fee payment: 18

Ref country code: ES

Payment date: 20230301

Year of fee payment: 18

Ref country code: CH

Payment date: 20230307

Year of fee payment: 18

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

Ref country code: SI

Payment date: 20230119

Year of fee payment: 18

Ref country code: SE

Payment date: 20230227

Year of fee payment: 18

Ref country code: PL

Payment date: 20230118

Year of fee payment: 18

Ref country code: IT

Payment date: 20230221

Year of fee payment: 18

Ref country code: GB

Payment date: 20230227

Year of fee payment: 18

Ref country code: DE

Payment date: 20230223

Year of fee payment: 18