EP2194155A1 - Hot-worked steel alloy - Google Patents

Hot-worked steel alloy Download PDF

Info

Publication number
EP2194155A1
EP2194155A1 EP09450215A EP09450215A EP2194155A1 EP 2194155 A1 EP2194155 A1 EP 2194155A1 EP 09450215 A EP09450215 A EP 09450215A EP 09450215 A EP09450215 A EP 09450215A EP 2194155 A1 EP2194155 A1 EP 2194155A1
Authority
EP
European Patent Office
Prior art keywords
elements
hot
steel alloy
nitrogen
silicon
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.)
Granted
Application number
EP09450215A
Other languages
German (de)
French (fr)
Other versions
EP2194155B1 (en
Inventor
Ingo Siller
Herbert Schweiger
Ziya Devrim Caliskanoglu
Silvia Zinner
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 and Co KG
Original Assignee
Boehler Edelstahl GmbH and Co KG
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 and Co KG filed Critical Boehler Edelstahl GmbH and Co KG
Priority to PL09450215T priority Critical patent/PL2194155T3/en
Priority to SI200930014T priority patent/SI2194155T1/en
Publication of EP2194155A1 publication Critical patent/EP2194155A1/en
Application granted granted Critical
Publication of EP2194155B1 publication Critical patent/EP2194155B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

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
    • C22C38/18—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
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C22C38/18—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

Definitions

  • the invention relates to a hot work steel alloy with high toughness and at the same time a high hardening depth or improved martensitic through hardenability in a thermal quenching of products such as die casting dies or extruded dies and the like.
  • a thermal tempering of a part for setting a high material hardness at service temperatures of the part up to 550 ° C and higher, essentially involves heating the material to a temperature at which it has a cubic face centered atomic structure or an austenitic structure, followed by forced cooling to obtain a Martensitge Stahl and a subsequent, optionally repeated tempering treatment at temperatures of mostly above 500 ° C.
  • the stresses formed in the material during cooling and microstructure are at least partially degraded in the material and, on the other hand, the material hardness is increased by carbide precipitations or a so-called secondary increase in hardness is achieved.
  • the properties of a material depend on its chemical composition and its microstructure set by a heat treatment, resulting in a certain property profile of a part.
  • the chemical composition of a material and the intensity of the cooling or the removal of heat from the surface during curing of the part determine the microstructure in the area of the surface and due to the reheating of the part inside the microstructure as a function of Distance to the sub-surface.
  • the respective local microstructure is decisive for the locally given material properties of the thermally tempered material.
  • Hot working materials for die-casting molds and the like are subject to increasing demands due to shortened press follow-up times and increased casting pressures due to increasingly economical production of the products. Furthermore, increasingly complex geometries of the mold cavities are provided so that summarily significantly increased total loads of the material are present. These overall stresses can cause tool failures due to stress cracking, fire cracking, coarse fracture, corrosion and erosion, requiring materials with high hardness and strength as well as high toughness and ductility. However, these required properties are dependent on the chemical composition of the alloy and the resulting tempering properties of the same.
  • the material no. 1.2343 is used for "highly stressed tools, dies and presses".
  • the above materials have a high hardening depth or a deep-reaching, thermal heat resistance to required hardness values between 50 and 55 HRC. However, their toughness properties are low, which can be detrimental to the performance characteristics of die casting molds.
  • the invention is now based on the object to provide a hot-work tool of the type mentioned, which forms a largely complete, martensitic microstructure at a forced cooling from the austenite even at low cooling, after which by a targeted tempering a high hardness and improved toughness of Material is achieved.
  • the advantage of the alloy composition according to the invention is essentially to be seen in the fact that the elements as a whole, in particular the elements silicon, molybdenum, vanadium and nitrogen are closely matched in terms of conversion kinetics, so that a desired strength and hardness with high toughness of the material in a thermal Compensation can be achieved with reduced cooling rate during curing.
  • a further substantial increase in the toughness properties of the tempered material can be achieved if the hot-work steel alloy has maximum concentrations of one or all elements in% by weight of Phosphorus (P) 0005 Sulfur (S) 0003 Nickel (Ni) 12:10 Tungsten (W) 12:10 Copper (Cu) 12:10 Cobalt (Co) 12:10 Titanium (Ti) 0008 Niobium (Nb) 12:03 Oxygen (O) 0003 Boron (B) 0001 Arsenic (As) 12:01 Tin (Sn) 0.0025 Antimony (Sb) 12:01 Zinc (Zn) 0001 Calcium (Ca) 0.0002 Magnesium (Mg) 0.0002 having.
  • the above elements can either form precipitates or compounds which are enriched in particular at the grain boundaries and thus reduce the toughness properties of the material abruptly from a concentration limit or they effect grain boundary occupancy, which act similarly unfavorable.
  • the hot-working steel alloy contains one or more of the alloying elements in% by weight.
  • Fig. 1 shows: notched impact values of the material after a thermal tempering as a function of the cooling parameters during the hardening treatment.
  • Cooling parameter [ ⁇ ] corresponds to the time [in sec.] For a cooling down from 800 ° C to 500 ° C broken by 100.
  • alloying elements of the materials listed in Table 1 the remainder being the content of iron and accompanying and impurity elements.
  • the materials no. 1.2343 with standard Si contents and no. 1.2367 have a lower toughness with a hardening hardness of 44 HRC, but have a considerable through hardenability, which is documented by only slightly decreasing toughness values depending on the cooling parameter.
  • an experimental alloy W 350 according to the invention shows slightly lower toughness values at room temperature in the state tempered to 44 HRC at high cooling rates or in the range of the cooling parameter ⁇ to 13 in comparison with the SO material No. 1.2343 (Si ⁇ 0.2% by weight); However, the viscosity of the material remains essentially unchanged at superior high values even with decreasing cooling rates or higher cooling parameters.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Contacts (AREA)

Abstract

The hot working steel alloy consists of alloy elements having carbon (0.37-0.40 wt.%), silicon (0.18-0.26 wt.%), manganese (0.50-0.58 wt.%), chromium (4.90-5.10 wt.%), molybdenum (1.65-1.80 wt.%), vanadium (0.52-0.60 wt.%), nitrogen (0.012-0.015 wt.%), phosphorus (0.005 wt.%), sulfur (0.003 wt.%), nickel (0.10 wt.%), tungsten (0.10 wt.%), copper (0.10 wt.%), cobalt (0.10 wt.%), titanium (0.008 wt.%), niobium (0.03 wt.%), oxygen (0.003 wt.%), boron (0.001 wt.%), arsenic (0.01 wt.%), tin (0.0025 wt.%) and/or antimony, and impurity elements and/or iron as remnant. The hot working steel alloy consists of alloy elements having carbon (0.37-0.40 wt.%), silicon (0.18-0.26 wt.%), manganese (0.50-0.58 wt.%), chromium (4.90-5.10 wt.%), molybdenum (1.65-1.80 wt.%), vanadium (0.52-0.60 wt.%), nitrogen (0.012-0.015 wt.%), phosphorus (0.005 wt.%), sulfur (0.003 wt.%), nickel (0.10 wt.%), tungsten (0.10 wt.%), copper (0.10 wt.%), cobalt (0.10 wt.%), titanium (0.008 wt.%), niobium (0.03 wt.%), oxygen (0.003 wt.%), boron (0.001 wt.%), arsenic (0.01 wt.%), tin (0.0025 wt.%), antimony (0.01 wt.%), zinc (0.001 wt.%), calcium (0.0002 wt.%) and/or magnesium (0.0002 wt.%) and impurity elements and/or iron as remnant.

Description

Die Erfindung bezieht sich auf eine Warmarbeitsstahl-Legierung mit hoher Zähigkeit und gleichzeitig großer Einhärttiefe bzw. verbesserter, martensitischer Durchhärtbarkeit bei einem thermischen Vergüten von Erzeugnissen wie beispielsweise Druckgießformen oder Strangpressmatrizen und dgl..The invention relates to a hot work steel alloy with high toughness and at the same time a high hardening depth or improved martensitic through hardenability in a thermal quenching of products such as die casting dies or extruded dies and the like.

Ein thermisches Vergüten eines Teiles, zB. aus Warmarbeitsstahl, zur Einstellung einer hohen Materialhärte bei Einsatztemperaturen des Teiles bis zu 550°C und höher beinhaltet im Wesentlichen ein Anwärmen des Werkstoffes auf eine Temperatur, bei welcher dieser eine kubisch-flächenzentrierte Atomstruktur bzw. ein austenitisches Gefüge hat, gefolgt von einer forcierten Abkühlung zur Erlangung eines Martensitgefüges und einer nachfolgenden, gegebenenfalls mehrmaligen Anlassbehandlung bei Temperaturen von zumeist über 500°C. Während des Anlassens werden einerseits die bei der Abkühlung und Gefügeumwandlung gebildeten Spannungen im Werkstoff zumindest teilweise abgebaut und andererseits durch Karbidausscheidungen die Materialhärte erhöht bzw. eine sog. sekundäre Härtesteigerung erreicht.A thermal tempering of a part, eg. hot work tool steel, for setting a high material hardness at service temperatures of the part up to 550 ° C and higher, essentially involves heating the material to a temperature at which it has a cubic face centered atomic structure or an austenitic structure, followed by forced cooling to obtain a Martensitgefüges and a subsequent, optionally repeated tempering treatment at temperatures of mostly above 500 ° C. During tempering, on the one hand, the stresses formed in the material during cooling and microstructure are at least partially degraded in the material and, on the other hand, the material hardness is increased by carbide precipitations or a so-called secondary increase in hardness is achieved.

Eine Umwandlung eines austentischen Gefüges in eine Martensitstruktur erfordert, wie dem Fachmann bekannt ist, eine Mindestabkühlgeschwindigkeit des Werkstoffes, weil diese Umwandlung aufgrund einer ausgeprägt hohen Unterkühlung als diffusionsloser Umklappprozess der Atomstruktur erfolgt. Niedrigere Abkühlraten führen zur Bildung eines Bainit- oder Perlit-Gefüges.Conversion of a Austentischen structure into a martensite structure requires, as is known in the art, a minimum cooling rate of the material, because this conversion is due to a pronounced high supercooling as a diffusion-free Umklappprozess the atomic structure. Lower cooling rates lead to the formation of a bainite or pearlite microstructure.

Die Eigenschaften eines Werkstoffes sind von dessen chemischer Zusammensetzung und von dessen durch eine Wärmebehandlung eingestellten Gefügestruktur abhängig und ergeben daraus ein bestimmtes Eigenschaftsprofil eines Teiles.The properties of a material depend on its chemical composition and its microstructure set by a heat treatment, resulting in a certain property profile of a part.

Mit anderen Worten: Die chemische Zusammensetzung eines Werkstoffes und die Intensität der Abkühlung bzw. der Wärmeabfuhr von der Oberfläche beim Härten des Teiles bestimmen die Gefügestruktur im Bereich der Oberfläche und aufgrund der Rückwärmung aus dem Teilinneren die Gefügeausbildung in Abhängigkeit vom Abstand zur Teiloberfläche. Die jeweilige örtliche Gefügestruktur ist für die örtlich gegebenen Materialeigenschaften des thermisch vergüteten Werkstoffes bestimmend.In other words, the chemical composition of a material and the intensity of the cooling or the removal of heat from the surface during curing of the part determine the microstructure in the area of the surface and due to the reheating of the part inside the microstructure as a function of Distance to the sub-surface. The respective local microstructure is decisive for the locally given material properties of the thermally tempered material.

Warmarbeitswerkstoffe für Druckgussformen und dgl. unterliegen aus Gründen einer zunehmend wirtschaftlichen Herstellung der Produkte steigenden Beanspruchungen durch verkürzte Pressfolgezeiten und erhöhte Gießdrücke. Weiters werden in steigendem Maße komplexe Geometrien der Formhohlräume vorgesehen, sodass summarisch wesentlich erhöhte Gesamtbelastungen des Werkstoffes vorliegen. Diese Gesamtbelastungen können Werkzeugausfälle durch Spannungsrisse, Brandrisse, Grobbruch, Korrosion und Erosion verursachen, sodass Werkstoffe mit hoher Härte und Festigkeit sowie gleichzeitig hoher Zähigkeit und Duktilität gefordert sind. Diese geforderten Eigenschaften sind jedoch von der chemischen Zusammensetzung der Legierung und der daraus resultierenden Vergüteeigenschaften derselben abhängig.Hot working materials for die-casting molds and the like are subject to increasing demands due to shortened press follow-up times and increased casting pressures due to increasingly economical production of the products. Furthermore, increasingly complex geometries of the mold cavities are provided so that summarily significantly increased total loads of the material are present. These overall stresses can cause tool failures due to stress cracking, fire cracking, coarse fracture, corrosion and erosion, requiring materials with high hardness and strength as well as high toughness and ductility. However, these required properties are dependent on the chemical composition of the alloy and the resulting tempering properties of the same.

Seit langem werden Cr-Mo-V-Stähle für Warmarbeitswerkzeuge verwendet, wobei die Stahlsorten X38 CrMoV 51 und X38 CrMoV 53 entsprechend DIN Stahl-Eisen-Liste Werkstoff Nr. 1.2343 und Werkstoff Nr. 1.2367, wie auch listenmäßig angegeben, "hochanlassbeständig" und für "Werkzeuge mit großen Abmessungen" geeignet sind.For a long time Cr-Mo-V-steels are used for hot work tools, the steel grades X38 CrMoV 51 and X38 CrMoV 53 according to DIN Steel-Iron-List material no. 1.2343 and material no. 1.2367, as stated in the list, "high-start resistant" and suitable for "tools with large dimensions".

Der Werkstoff Nr. 1.2343 dient für "hochbeanspruchte Werkzeuge, Gesenke und Pressen".The material no. 1.2343 is used for "highly stressed tools, dies and presses".

Obige Werkstoffe weisen eine große Einhärttiefe bzw. eine tiefreichende, thermische Vergütbarkeit auf geforderte Härtewerte zwischen 50 und 55 HRC auf. Allerdings sind deren Zähigkeitseigenschaften gering, was nachteilig für die Gebrauchseigenschaften von Druckgussformen sein kann.The above materials have a high hardening depth or a deep-reaching, thermal heat resistance to required hardness values between 50 and 55 HRC. However, their toughness properties are low, which can be detrimental to the performance characteristics of die casting molds.

Bei einem Werkstoff Nr. 1.2343 kann durch ein Absenken des vorgesehenen Siliciumgehaltes von 0.90 bis 1.20 Gew.-% auf eine Konzentration um 0.2 Gew.-% eine wesentliche Erhöhung der Materialzähigkeit nach einer Vergütebehandlung erreicht werden, allerdings sind dafür hohe Abkühlgeschwindigkeiten beim Härten erforderlich, die oftmals nicht erreicht werden können.With a material no. 1.2343 can be achieved by a lowering of the intended silicon content of 0.90 to 1.20 wt .-% to a concentration of 0.2 wt .-%, a substantial increase in material toughness after a heat treatment, but are high cooling rates for curing necessary, which often can not be achieved.

Die Erfindung setzt sich nun zum Ziel, einen Warmarbeitsstahl der eingangs genannten Art zu schaffen, welcher bei einer forcierten Abkühlung aus dem Austenitgebiet auch bei niedrigen Abkühlraten eine weitgehend vollständige, martensitische Gefügestruktur bildet, wonach durch eine gezielte Anlassbehandlung eine hohe Härte- und verbesserte Zähigkeit des Werkstoffes erreicht wird.The invention is now based on the object to provide a hot-work tool of the type mentioned, which forms a largely complete, martensitic microstructure at a forced cooling from the austenite even at low cooling, after which by a targeted tempering a high hardness and improved toughness of Material is achieved.

Diese Ziel wird bei einer Warmarbeitsstahl-Legierung dadurch erreicht, dass die Legierungselemente Gehalte in Gew.-% von Kohlenstoff (C) 0.35 bis 0.42 Silicium (Si) 0.15 bis 0.29 Mangan (Mn) 0.40 bis 0.70 Chrom (Cr) 4.70 bis 5.45 Molybdän (Mo) 1.55 bis 1.95 Vanadin (V) 0.40 bis 0.75 Stickstoff (N) 0.011 bis 0.016 Eisen (Fe) und Verunreinigungselemente als Rest
aufweisen.This goal is achieved in a hot-work steel alloy in that the alloying elements contents in wt .-% of Carbon (C) 12:35 to 12:42 Silicon (Si) 12:15 to 12:29 Manganese (Mn) 12:40 to 0.70 Chrome (Cr) 4.70 to 5:45 Molybdenum (Mo) 1:55 to 1.95 Vanadin (V) 12:40 to 0.75 Nitrogen (N) 0011 to 0016 Iron (Fe) and impurity elements as rest
exhibit.

Der Vorteil der erfindungsgemäßen Legierungszusammensetzung ist im Wesentlichen darin zu sehen, dass die Elemente insgesamt, insbesondere die Elemente Silicium, Molybdän, Vanadin und Stickstoff, in engen Grenzen umwandlungskinetisch aufeinander abgestimmt sind, sodass eine gewünschte Festigkeit und Härte bei hoher Zähigkeit des Werkstoffes bei einer thermischen Vergütung mit verminderter Abkühlrate beim Härten erreicht werden kann.The advantage of the alloy composition according to the invention is essentially to be seen in the fact that the elements as a whole, in particular the elements silicon, molybdenum, vanadium and nitrogen are closely matched in terms of conversion kinetics, so that a desired strength and hardness with high toughness of the material in a thermal Compensation can be achieved with reduced cooling rate during curing.

Dadurch ist es möglich, entweder größere Eindringtiefen eines für die mechanischen Eigenschaften des Teiles günstigen, martensitischen Härtegefüges bei einer gegebenen Abkühlgeschwindigkeit zu erreichen oder mit Vorteil eine niedrigere Abkühlrate bei einer Härtung zu verwenden und dadurch die Härtespannungen im vielfach mit einer Gravur bzw. mit einer Negativform des Gussteiles versehenen Druckgießform zu minimieren. Dies ist von besonderer Bedeutung, weil im zunehmendem Maße ein sogenanntes Vakuumhärten von Formteilen verwendet wird, wobei auch aus Gründen der Vermeidung von Oxidationen und Entkohlung der bearbeiteten Oberfläche des Werkstückes bzw. der Form bei einer Austenitisierung eine Anwärmung im Vakuum erfolgt, wonach eine forcierte Abkühlung mit einem Stickstoff-Gasstrom durchgeführt wird. Für diese Art der Härtung eines Teiles hat sich eine erfindungsgemäß chemisch zusammengesetzte Legierung besonders bewährt.This makes it possible either to achieve greater penetration depths of a martensitic hardening structure favorable for the mechanical properties of the part at a given cooling rate, or advantageously to use a lower cooling rate during hardening and thus in many cases engraving or with a negative mold to minimize casting of the die. This is of particular importance because so-called vacuum hardening of molded parts is increasingly used is carried out, wherein also for reasons of avoiding oxidation and decarburization of the machined surface of the workpiece or the mold in an austenitization, a heating in vacuo, after which a forced cooling is carried out with a nitrogen gas stream. For this type of curing of a part, an inventively chemically combined alloy has proven particularly useful.

Eine weitere wesentliche Steigerung der Zähigkeitseigenschaften des vergüteten Werkstoffes kann erreicht werden, wenn die Warmarbeitsstahl-Legierung maximale Konzentrationen ein oder sämtlicher Elemente in Gew.-% von Phosphor (P) 0.005 Schwefel (S) 0.003 Nickel (Ni) 0.10 Wolfram (W) 0.10 Kupfer (Cu) 0.10 Cobalt (Co) 0.10 Titan (Ti) 0.008 Niob (Nb) 0.03 Sauerstoff (O) 0.003 Bor (B) 0.001 Arsen (As) 0.01 Zinn (Sn) 0.0025 Antimon (Sb) 0.01 Zink (Zn) 0.001 Calcium (Ca) 0.0002 Magnesium (Mg) 0.0002 aufweist.A further substantial increase in the toughness properties of the tempered material can be achieved if the hot-work steel alloy has maximum concentrations of one or all elements in% by weight of Phosphorus (P) 0005 Sulfur (S) 0003 Nickel (Ni) 12:10 Tungsten (W) 12:10 Copper (Cu) 12:10 Cobalt (Co) 12:10 Titanium (Ti) 0008 Niobium (Nb) 12:03 Oxygen (O) 0003 Boron (B) 0001 Arsenic (As) 12:01 Tin (Sn) 0.0025 Antimony (Sb) 12:01 Zinc (Zn) 0001 Calcium (Ca) 0.0002 Magnesium (Mg) 0.0002 having.

Obige Elemente können entweder Ausscheidungen oder Verbindungen bilden, welche insbesondere an den Korngrenzen angereichert sind und derart die Zähigkeitseigenschaften des Werkstoffes sprunghaft ab einer Konzentrationsgrenze erniedrigen oder sie bewirken Korngrenzenbelegungen, die gleichartig ungünstig wirken.The above elements can either form precipitates or compounds which are enriched in particular at the grain boundaries and thus reduce the toughness properties of the material abruptly from a concentration limit or they effect grain boundary occupancy, which act similarly unfavorable.

Durch eine in sehr engen Grenzen eingestellte, chemische Zusammensetzung des erfindungsgemäßen Werkstoffes nach einer bevorzugten Ausführungsform desselben enthält die Warmarbeitsstahl-Legierung ein oder mehrere der Legierungselemente in Gew.-% Kohlenstoff (C) 0.37 bis 0.40 Silicium (Si) 0.16 bis 0.28, vorzugsweise 0.18 bis 0.25 Mangan (Mn) 0.45 bis 0.60, vorzugsweise 0.50 bis 0.58 Chrom (Cr) 4.80 bis 5.20, vorzugsweise 4.90 bis 5.10 Molybdän (Mo) 1.50 bis 1.90, vorzugsweise 1.65 bis 1.80 Vanadin (V) 0.45 bis 0.70, vorzugsweise 0.52 bis 0.60 Stickstoff (N) 0.012 bis 0.015 Eisen (Fe) und Verunreinigungselemente als Rest.By means of a chemical composition of the material according to the invention set in very narrow limits according to a preferred embodiment thereof, the hot-working steel alloy contains one or more of the alloying elements in% by weight. Carbon (C) 12:37 to 12:40 Silicon (Si) 12:16 to 0:28, preferably 12:18 to 12:25 Manganese (Mn) 12:45 to 0.60, preferably 12:50 to 12:58 Chrome (Cr) 4.80 to 5:20, preferably 4.90 to 5.10 Molybdenum (Mo) 1:50 to 1.90, preferably 1.65 to 1.80 Vanadin (V) 12:45 to 0.70 preferably 12:52 to 0.60 Nitrogen (N) 0012 to 0015 Iron (Fe) and impurity elements as rest.

Mittels dieser durch besonders enge Grenzen in der chemischen Zusammensetzung gekennzeichneten, erfindungsgemäßen Legierung, welche besondere Anforderungen an eine Erschmelzungstechnologie stellt, ist es möglich, hohe Zähigkeitswerte des Werkstoffes auch bei niedrigen Abkühlungsraten im thermischen Vergütungsverfahren bei hohen Materialhärten zu erreichen.By means of this invention characterized by particularly narrow limits in the chemical composition, alloy according to the invention, which makes special demands on a melting technology, it is possible to achieve high toughness values of the material even at low cooling rates in the thermal annealing process with high material hardness.

Im Folgenden soll die Erfindung anhand von Untersuchungsergebnissen näher erläutert werden.In the following, the invention will be explained in more detail on the basis of examination results.

Hilfsweise sind die Untersuchungsergebnisse in Fig. 1 zusammengefasst.In the alternative, the test results are in Fig. 1 summarized.

Fig. 1 zeigt: Kerbschlagzähigkeitswerte des Werkstoffes nach einer thermischen Vergütung in Abhängigkeit von den Abkühlparametern bei der Härtebehandlung. Fig. 1 shows: notched impact values of the material after a thermal tempering as a function of the cooling parameters during the hardening treatment.

Legierungen mit einer chemischen Zusammensetzung gemäß der Erfindung und nach DIN Werkstoff Nr. 1.2343 mit normgerechten und mit abgesenkten Si-Gehalten sowie nach DIN Werkstoff Nr. 1.2367, wie in Tab. 1 angegeben, wurden nach einer thermischen Vergütebehandlung auf eine Materialhärt von 44 HRC mit unterschiedlichen Abkühlparametern λ beim Härten untersucht. Dabei wird der Wert, der den Parameter λ kennzeichnet, wie folgt berechnet:
Abkühlparameter [λ] entspricht der Zeit [in sec.] für eine Abkühlung von 800°C auf 500°C gebrochen durch 100.
Nachfolgend sind die in Tab. 1 aufgelisteten Legierungselemente der Werkstoffe genannt, wobei der Rest den Gehalt an Eisen und Begleit- sowie Verunreinigungselementen darstellt.Alloys with a chemical composition according to the invention and according to DIN material no. 1.2343 with standardized and with lowered Si contents as well as according to DIN material no. 1.2367, as indicated in Tab. 1, were after a heat treatment to a material hardness of 44 HRC with investigated different cooling parameters λ during curing. The value that characterizes the parameter λ is calculated as follows:
Cooling parameter [λ] corresponds to the time [in sec.] For a cooling down from 800 ° C to 500 ° C broken by 100.
Listed below are the alloying elements of the materials listed in Table 1, the remainder being the content of iron and accompanying and impurity elements.

Legierungszusammensetzung in Gew.-%Alloy composition in% by weight

Werkstoff Nr.Material number. CC SiSi MnMn PP SS NN CrCr MoNot a word NiNi VV 1.23431.2343 0.3912:39 1.111.11 0.4112:41 0.0210021 0.0230023 -- 5.285.28 1.261.26 0.2112:21 0.3812:38 1.2343 So1.2343 Sun 0.3812:38 0.2112:21 0.3912:39 0.0220022 0.0190019 -- 5.345:34 1.301.30 0.1612:16 0.4012:40 1.23671.2367 0.3812:38 0.4012:40 0.4712:47 0.0290029 0.0210021 -- 5.005:00 2.982.98 0.2012:20 0.610.61 W 350W 350 0.3912:39 0.1912:19 0.5112:51 0.0040004 0.0010001 0.0130013 4.914.91 1.691.69 0.0612:06 0.5312:53

Fig. 1 zeigt, dass mit einem Abkühlparameter bis ca. λ = 12 der Werkstoff Nr. 1.2343 mit Si-Gehalten abgesenkt auf ca. 0.20 Gew.-% im auf eine Materialhärte von 44 HRC thermisch vergüteten Zustand die höchste Zähigkeit gemessen nach Charpy-V hat. Allerdings fallen in der Folge mit steigendem Abkühlparameter λ die Zähigkeitswerte sprunghaft auf niedriges Niveau ab. Fig. 1 shows that with a cooling parameter to about λ = 12, the material no. 1.2343 with Si contents lowered to about 0.20 wt .-% in a material hardness of 44 HRC thermally tempered state has the highest toughness measured according to Charpy-V. However, as the cooling parameter λ increases, the toughness values suddenly drop to a low level.

Die Werkstoffe Nr. 1.2343 mit normgerechten Si-Gehalten und Nr. 1.2367 weisen bei einer Vergütungshärte von 44 HRC eine geringere Zähigkeit auf, haben jedoch eine beachtliche Durchhärtbarkeit, was sich durch nur geringfügig sinkende Zähigkeitswerte in Abhängigkeit vom Abkühlparameter dokumentiert.The materials no. 1.2343 with standard Si contents and no. 1.2367 have a lower toughness with a hardening hardness of 44 HRC, but have a considerable through hardenability, which is documented by only slightly decreasing toughness values depending on the cooling parameter.

Eine erfindungsgemäße Versuchslegierung W 350 zeigt zwar bei hohen Abkühlraten bzw. im Bereich des Abkühlparameters λ bis 13 im Vergleich mit den So-Werkstoff Nr. 1.2343 (Si ≈ 0.2 Gew.-%) etwas geringere Zähigkeitswerte bei Raumtemperatur im auf 44 HRC vergüteten Zustand; die Zähigkeit des Werkstoffes bleibt jedoch auch bei sinkenden Abkühlraten bzw. höheren Abkühlparametern im Wesentlichen unverändert auf überlegen hohen Werten.Although an experimental alloy W 350 according to the invention shows slightly lower toughness values at room temperature in the state tempered to 44 HRC at high cooling rates or in the range of the cooling parameter λ to 13 in comparison with the SO material No. 1.2343 (Si ≈ 0.2% by weight); However, the viscosity of the material remains essentially unchanged at superior high values even with decreasing cooling rates or higher cooling parameters.

Claims (3)

Warmarbeitsstahl-Legierung, enthaltend die Elemente Kohlenstoff (C), Silicium (Si), Mangan (Mn), Chrom (Cr), Molybdän (Mo), Vanadin (V), Stickstoff (N) und Verunreinigungselemente sowie Eisen als Rest, mit der Maßgabe, dass die Legierungselemente Gehalte in Gew.-% von Kohlenstoff (C) 0.35 bis 0.42 Silicium (Si) 0.15 bis 0.29 Mangan (Mn) 0.40 bis 0.70 Chrom (Cr) 4.70 bis 5.45 Molybdän (Mo) 1.55 bis 1.95 Vanadin (V) 0.40 bis 0.75 Stickstoff (N) 0.011 bis 0.016 aufweisen.
Hot-work steel alloy containing the elements carbon (C), silicon (Si), manganese (Mn), chromium (Cr), molybdenum (Mo), vanadium (V), nitrogen (N) and impurity elements, and iron as balance, with Provided that the alloying elements contents in wt .-% of Carbon (C) 12:35 to 12:42 Silicon (Si) 12:15 to 12:29 Manganese (Mn) 12:40 to 0.70 Chrome (Cr) 4.70 to 5:45 Molybdenum (Mo) 1:55 to 1.95 Vanadin (V) 12:40 to 0.75 Nitrogen (N) 0011 to 0016 exhibit.
Warmarbeitsstahl-Legierung nach Anspruch 1, enthaltend maximale Konzentrationen ein oder sämtlicher Elemente in Gew.-% von Phosphor (P) 0.005 Schwefel (S) 0.003 Nickel (Ni) 0.10 Wolfram (W) 0.10 Kupfer (Cu) 0.10 Cobalt (Co) 0.10 Titan (Ti) 0.008 Niob (Nb) 0.03 Sauerstoff (O) 0.003 Bor (B) 0.001 Arsen (As) 0.01 Zinn (Sn) 0.0025 Antimon (Sb) 0.01 Zink (Zn) 0.001 Calcium (Ca) 0.0002 Magnesium (Mg) 0.0002
A hot working steel alloy according to claim 1, containing maximum concentrations of one or all elements in% by weight of Phosphorus (P) 0005 Sulfur (S) 0003 Nickel (Ni) 12:10 Tungsten (W) 12:10 Copper (Cu) 12:10 Cobalt (Co) 12:10 Titanium (Ti) 0008 Niobium (Nb) 12:03 Oxygen (O) 0003 Boron (B) 0001 Arsenic (As) 12:01 Tin (Sn) 0.0025 Antimony (Sb) 12:01 Zinc (Zn) 0001 Calcium (Ca) 0.0002 Magnesium (Mg) 0.0002
Warmarbeitsstahl-Legierung nach Anspruch 1 oder 2, enthaltend ein oder mehrere der Legierungselemente in Gew.-% Kohlenstoff (C) 0.37 bis 0.40 Silicium (Si) 0.16 bis 0.28, vorzugsweise 0.18 bis 0.25 Mangan (Mn) 0.45 bis 0.60, vorzugsweise 0.50 bis 0.58 Chrom (Cr) 4.80 bis 5.20, vorzugsweise 4.90 bis 5.10 Molybdän (Mo) 1.50 bis 1.90, vorzugsweise 1.65 bis 1.80 Vanadin (V) 0.45 bis 0.70, vorzugsweise 0.52 bis 0.60 Stickstoff (N) 0.012 bis 0.015
Eisen (Fe) und Verunreinigungselemente als Rest.Hot-work steel alloy according to claim 1 or 2, containing one or more of the alloying elements in% by weight Carbon (C) 12:37 to 12:40 Silicon (Si) 12:16 to 0:28, preferably 12:18 to 12:25 Manganese (Mn) 12:45 to 0.60, preferably 12:50 to 12:58 Chrome (Cr) 4.80 to 5:20, preferably 4.90 to 5.10 Molybdenum (Mo) 1:50 to 1.90, preferably 1.65 to 1.80 Vanadin (V) 12:45 to 0.70 preferably 12:52 to 0.60 Nitrogen (N) 0012 to 0015
Iron (Fe) and impurity elements as rest.
EP09450215A 2008-11-20 2009-11-16 Hot-worked steel alloy Active EP2194155B1 (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL09450215T PL2194155T3 (en) 2008-11-20 2009-11-16 Hot-worked steel alloy
SI200930014T SI2194155T1 (en) 2008-11-20 2009-11-16 Hot-worked steel alloy

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
AT0181508A AT506790B1 (en) 2008-11-20 2008-11-20 HOT STEEL ALLOY

Publications (2)

Publication Number Publication Date
EP2194155A1 true EP2194155A1 (en) 2010-06-09
EP2194155B1 EP2194155B1 (en) 2010-11-10

Family

ID=41402020

Family Applications (1)

Application Number Title Priority Date Filing Date
EP09450215A Active EP2194155B1 (en) 2008-11-20 2009-11-16 Hot-worked steel alloy

Country Status (11)

Country Link
US (2) US20100150772A1 (en)
EP (1) EP2194155B1 (en)
AT (2) AT506790B1 (en)
AU (1) AU2009238307C1 (en)
BR (1) BRPI0904501A2 (en)
CA (1) CA2686071C (en)
DE (1) DE502009000171D1 (en)
ES (1) ES2353192T3 (en)
PL (1) PL2194155T3 (en)
SI (1) SI2194155T1 (en)
ZA (1) ZA200908201B (en)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3050649A1 (en) 2015-01-28 2016-08-03 Daido Steel Co.,Ltd. Steel powder and mold using the same
CN107400833A (en) * 2017-08-30 2017-11-28 王延敏 A kind of steel construction jacking system manufacturing process
WO2020070917A1 (en) 2018-10-05 2020-04-09 日立金属株式会社 Hot work tool steel and hot work tool

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AT507215B1 (en) * 2009-01-14 2010-03-15 Boehler Edelstahl Gmbh & Co Kg WEAR-RESISTANT MATERIAL
SE539646C2 (en) * 2015-12-22 2017-10-24 Uddeholms Ab Hot work tool steel
CN109821951B (en) * 2018-12-06 2020-07-21 苏州普热斯勒先进成型技术有限公司 Preparation method and device of corrosion-resistant hot stamping part

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0733719A1 (en) * 1995-03-23 1996-09-25 BÖHLER Edelstahl GmbH Iron base alloy for use at high temperature
EP0939140A1 (en) * 1998-02-27 1999-09-01 BÖHLER Edelstahl GmbH Steel for use at high temperatures
EP1300482A1 (en) * 2001-10-03 2003-04-09 BÖHLER Edelstahl GmbH Hot-work tool-steel article

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2893902A (en) * 1959-02-04 1959-07-07 Vanadium Alloys Steel Co Heat treatment of steel
US3791819A (en) * 1968-11-12 1974-02-12 Jones & Laughlin Steel Corp Production of stainless steels
JPH08269625A (en) * 1995-03-31 1996-10-15 Sumitomo Metal Ind Ltd Hot rolled tool steel excellent in high temperature strength and toughness
SE511758C2 (en) * 1998-03-27 1999-11-22 Uddeholm Tooling Ab Steel material for hot work tools
EP2065483A4 (en) * 2006-09-15 2016-03-23 Hitachi Metals Ltd Hot-working tool steel having excellent stiffness and high-temperature strength and method for production thereof

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0733719A1 (en) * 1995-03-23 1996-09-25 BÖHLER Edelstahl GmbH Iron base alloy for use at high temperature
EP0939140A1 (en) * 1998-02-27 1999-09-01 BÖHLER Edelstahl GmbH Steel for use at high temperatures
EP1300482A1 (en) * 2001-10-03 2003-04-09 BÖHLER Edelstahl GmbH Hot-work tool-steel article

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
SCHNEIDER R. ET AL: "EFFECTS OF DIFFERENT ALLOYING ELEMENTS ON THE HARDNESS PROFILE OF NITRIDED HOT-WORK TOOL STEELS", BHM BERG- UND HÜTTENMÄNNISCHE MONATSHEFTE, vol. 151, no. 3, 1 March 2006 (2006-03-01) - 31 March 2006 (2006-03-31), pages 105 - 109, XP002574215, ISSN: 0005-8912, DOI: 10.1007/BF03165181 *

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3050649A1 (en) 2015-01-28 2016-08-03 Daido Steel Co.,Ltd. Steel powder and mold using the same
US10975460B2 (en) 2015-01-28 2021-04-13 Daido Steel Co., Ltd. Steel powder and mold using the same
CN107400833A (en) * 2017-08-30 2017-11-28 王延敏 A kind of steel construction jacking system manufacturing process
WO2020070917A1 (en) 2018-10-05 2020-04-09 日立金属株式会社 Hot work tool steel and hot work tool
EP4230759A1 (en) 2018-10-05 2023-08-23 Proterial, Ltd. Hot work tool steel and hot work tool

Also Published As

Publication number Publication date
ES2353192T3 (en) 2011-02-28
AU2009238307B2 (en) 2013-12-19
CA2686071C (en) 2014-01-28
AU2009238307A1 (en) 2010-06-03
AT506790A4 (en) 2009-12-15
EP2194155B1 (en) 2010-11-10
BRPI0904501A2 (en) 2011-02-08
DE502009000171D1 (en) 2010-12-23
AT506790B1 (en) 2009-12-15
PL2194155T3 (en) 2011-04-29
SI2194155T1 (en) 2011-01-31
ZA200908201B (en) 2011-02-23
CA2686071A1 (en) 2010-05-20
ATE487805T1 (en) 2010-11-15
US20150292067A1 (en) 2015-10-15
AU2009238307C1 (en) 2014-03-13
US20100150772A1 (en) 2010-06-17

Similar Documents

Publication Publication Date Title
EP2253398B1 (en) Wear-resistant material
EP2446064B1 (en) Method for producing a hot press hardened component and use of a steel product for producing a hot press hardened component
EP3228724B1 (en) Tool steel, in particular hot-work steel, and steel object
EP2194155B1 (en) Hot-worked steel alloy
EP2875926B1 (en) Method for the production of plastic moulds made from martensitic chromium steel and plastic mould
EP3168312B1 (en) Engineering steel with bainitic structure, forged part produced therefrom and method for making a forged part
DE102017131218A1 (en) A method of making an article from a maraging steel
EP1249511B1 (en) High speed steel with good high temperature strength manufactured by powder metallurgy
DE202014101693U1 (en) Ring-shaped tool
EP1300482B1 (en) Hot-work tool-steel article
DE2800444C2 (en) Use of a Cr-Mo steel
WO2020058269A1 (en) Steel for surface hardening with high edge hardness and with a fine ductile core structure
EP1647606A1 (en) High hardness and wear resistant nickel based alloy for use as high temperature tooling
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
EP2396440A1 (en) Steel alloy
EP3225702B1 (en) Steel with reduced density and method for producing a steel flat or long product made from such steel
EP1471160B1 (en) Cold-worked Steel Object
EP1918401B1 (en) Steel alloy for machining tools
EP1445339B1 (en) Alloy and article with high heat resistance and high heat stability
AT500728B1 (en) Cutting tool, especially wood chipper blade, comprises an iron alloy containing defined amounts of carbon, silicon, manganese, sulfur, chromium, molybdenum, nickel, vanadium, tungsten and aluminum
DE4334062A1 (en) Tool steel compsn. having high temp. strength - comprises manganese@, chromium@, molybdenum@, tungsten@, vanadium@, cobalt@ and nitrogen@
DE102021101105A1 (en) Process for producing a tool steel as a carrier for PVD coatings and a tool steel
EP2824212B1 (en) Hot-working steel
DE1242376B (en) Use of a martensite-hardenable nickel-cobalt-molybdenum steel alloy

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 HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

AX Request for extension of the european patent

Extension state: AL BA RS

17P Request for examination filed

Effective date: 20100601

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/22 20060101AFI20100629BHEP

Ipc: C22C 38/24 20060101ALI20100629BHEP

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 HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM 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

Ref country code: CH

Ref legal event code: NV

Representative=s name: BUECHEL, VON REVY & PARTNER

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: 502009000171

Country of ref document: DE

Date of ref document: 20101223

Kind code of ref document: P

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: NL

Ref legal event code: T3

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Effective date: 20110216

LTIE Lt: invalidation of european patent or patent extension

Effective date: 20101110

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

Ref country code: NO

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: 20110210

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: 20101110

REG Reference to a national code

Ref country code: PL

Ref legal event code: T3

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: 20110210

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: 20101110

Ref country code: FI

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: 20101110

Ref country code: HR

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: 20101110

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: 20110310

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: 20110310

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: 20101110

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: MC

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

Effective date: 20101130

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: 20110211

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

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: 20101110

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: 20101110

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: 20101110

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: 20101110

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: 20101110

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

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

26N No opposition filed

Effective date: 20110811

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502009000171

Country of ref document: DE

Effective date: 20110811

BERE Be: lapsed

Owner name: BOHLER EDELSTAHL GMBH & CO KG

Effective date: 20111130

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: 20111130

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: 20110511

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

Ref country code: MK

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: 20101110

Ref country code: MT

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: 20101110

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

Ref country code: SM

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: 20101110

Ref country code: SE

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

Effective date: 20101117

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

Ref country code: LU

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

Effective date: 20101116

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: 20101110

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 7

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 8

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230706

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

Ref country code: NL

Payment date: 20231126

Year of fee payment: 15

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

Ref country code: GB

Payment date: 20231127

Year of fee payment: 15

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

Ref country code: ES

Payment date: 20231201

Year of fee payment: 15

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

Ref country code: TR

Payment date: 20231106

Year of fee payment: 15

Ref country code: SI

Payment date: 20231102

Year of fee payment: 15

Ref country code: SE

Payment date: 20231127

Year of fee payment: 15

Ref country code: IT

Payment date: 20231122

Year of fee payment: 15

Ref country code: FR

Payment date: 20231127

Year of fee payment: 15

Ref country code: DE

Payment date: 20231129

Year of fee payment: 15

Ref country code: CH

Payment date: 20231201

Year of fee payment: 15

Ref country code: AT

Payment date: 20231102

Year of fee payment: 15

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

Ref country code: PL

Payment date: 20231102

Year of fee payment: 15