EP1471160B1 - Cold-worked Steel Object - Google Patents
Cold-worked Steel Object Download PDFInfo
- Publication number
- EP1471160B1 EP1471160B1 EP04450082A EP04450082A EP1471160B1 EP 1471160 B1 EP1471160 B1 EP 1471160B1 EP 04450082 A EP04450082 A EP 04450082A EP 04450082 A EP04450082 A EP 04450082A EP 1471160 B1 EP1471160 B1 EP 1471160B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- less
- maximum
- cold
- steel object
- worked steel
- 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.)
- Expired - Lifetime
Links
- 229910000831 Steel Inorganic materials 0.000 title claims description 13
- 239000010959 steel Substances 0.000 title claims description 13
- 239000000463 material Substances 0.000 claims description 46
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 14
- 239000000843 powder Substances 0.000 claims description 13
- 239000011572 manganese Substances 0.000 claims description 12
- 239000011651 chromium Substances 0.000 claims description 10
- 239000010941 cobalt Substances 0.000 claims description 10
- 229910017052 cobalt Inorganic materials 0.000 claims description 10
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 10
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims description 9
- 239000011733 molybdenum Substances 0.000 claims description 9
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 9
- 229910052721 tungsten Inorganic materials 0.000 claims description 9
- 239000010937 tungsten Substances 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 8
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 239000010949 copper Substances 0.000 claims description 8
- 229910052760 oxygen Inorganic materials 0.000 claims description 8
- 239000001301 oxygen Substances 0.000 claims description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 239000010703 silicon Substances 0.000 claims description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 6
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 5
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 5
- 229910052751 metal Inorganic materials 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 239000011574 phosphorus Substances 0.000 claims description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 239000011669 selenium Substances 0.000 claims description 4
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 238000010310 metallurgical process Methods 0.000 claims description 3
- 239000000126 substance Substances 0.000 claims description 3
- BUGBHKTXTAQXES-UHFFFAOYSA-N Selenium Chemical compound [Se] BUGBHKTXTAQXES-UHFFFAOYSA-N 0.000 claims description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 2
- 229910052787 antimony Inorganic materials 0.000 claims description 2
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 claims description 2
- 229910052785 arsenic Inorganic materials 0.000 claims description 2
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 claims description 2
- 229910052797 bismuth Inorganic materials 0.000 claims description 2
- 239000000155 melt Substances 0.000 claims description 2
- 229910052711 selenium Inorganic materials 0.000 claims description 2
- 239000005864 Sulphur Substances 0.000 claims 2
- 239000004411 aluminium Substances 0.000 claims 2
- 238000003723 Smelting Methods 0.000 claims 1
- 230000001143 conditioned effect Effects 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 238000004519 manufacturing process Methods 0.000 description 9
- 238000012360 testing method Methods 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 7
- 229910000822 Cold-work tool steel Inorganic materials 0.000 description 5
- 229910000997 High-speed steel Inorganic materials 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 238000005452 bending Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- 230000002349 favourable effect Effects 0.000 description 3
- 230000007774 longterm Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 239000011593 sulfur Substances 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910000735 Pm alloy Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000000356 contaminant Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000004049 embossing Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000000873 masking effect Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 239000012925 reference material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
- C22C38/02—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
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
-
- 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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
Definitions
- the invention relates to a cold work tool steel article. More precisely, the invention relates to a cold work tool steel article with improved property profile, in particular with high strength and high ductility.
- the carbon content is aligned with the sum of the carbide formers in the alloy to both form carbides and to determine the hardenability and desired properties of the matrix. Concentrations of carbon of more than 0.6% by weight are required to achieve high hardness values of the matrix at the intended maximum contents of the carbide-forming elements during tempering, whereas contents of less than 1.0% by weight are important in order to obtain a to set the desired amount of carbide and carbide morphology.
- the vanadium content of the alloy in wt .-% is greater than 1.0, but less than 2.9, on the one hand to represent sufficient monocarbides and on the other hand enough secondary hardness potential.
- the secondary hardness potential must be seen with a residual vanadium and the contents of the elements molybdenum (Mo) and tungsten (W), because by concentrations in wt .-% of 3.8 molybdenum (Mo), and 3.4 tungsten (W ) and larger already causes a deterioration of the matrix toughness, whereas larger contents than 1.9 molybdenum (Mo) and 1.8 tungsten (W) are required for an advantageous vanadium masking in order to avoid large sharp-edged monocarbides.
- the molybdenum content is at most 10% greater than that of tungsten (W).
- Abrasion wear was tested with SiC abrasive paper P 120.
- the alloy according to the invention has a very good abrasive wear resistance, which was determined in the SiC abrasive paper test. This property was achieved despite a reduced primary carbide content compared to standard PM alloys used in this field of application.
Description
Die Erfindung betrifft einen Kaltarbeitsstahl-Gegenstand. Näher präzisiert bezieht sich die Erfindung auf einen Kaltarbeitsstahl-Gegenstand mit verbessertem Eigenschaftsprofil, insbesondere mit hoher Festigkeit sowie hoher Duktilität.The invention relates to a cold work tool steel article. More precisely, the invention relates to a cold work tool steel article with improved property profile, in particular with high strength and high ductility.
Für eine Kaltmassivumformung, beispielsweise mit Fließpressmatrizen und Stempel zur Herstellung von Bauteilen und auch für Schneidwerkzeuge mit zusätzlich hohen Anforderungen an die Werkstoffzähigkeit, wie Gewindebohrer und dergleichen, werden in der modernen Technik Gegenstände mit insgesamt hohem Material-Eigenschaftsniveau benötigt. Solche Kaltarbeitstähle sind zum Beispiel aus JP 7316739 bekannt. Dies ergibt sich auch aus den Aufwendungen, die für die Wekzeugherstellung anfallen, weil eine komplizierte Geometrie eines zu fertigenden Bauteiles zumeist hohe Kosten für eine Werkzeugherstellung bedingen.For a cold massive forming, for example, with extrusion dies and punches for the production of components and also for cutting tools with additional high demands on the material toughness, such as taps and the like, in modern art objects with a high overall material property level are needed. Such cold work steels are known, for example, from JP 7316739. This also results from the expenses incurred for the manufacture of tools, because a complicated geometry of a component to be manufactured usually entail high costs for tool production.
Dieses Erfordernis ist in erster Linie im Hinblick auf eine verbesserte Wirtschaftlichkeit bei einer Großzahl-Herstellung von Bauteilen oder Komponenten zu sehen. Um die Gesamtkosten gering zu halten, soll somit für den jeweiligen Bedarfsfall eine Werkstoffauswahl für das Teil getroffen werden, welche auf Grund der Materialeigenschaften eine höchstmögliche Lebensdauer desselben erreichen lässt.This requirement is primarily to be seen in terms of improved economics in a large number of components or components. In order to keep the overall costs low, a selection of materials for the part should therefore be made for the particular case of need, which can achieve the highest possible service life of the same due to the material properties.
Zur Verbesserung der Standzeit eines Kaltarbeitsstahl-Gegenstandes im Einsatz mit insgesamt hoher Beanspruchung sind gleichermaßen die Materialeigenschaften Duktilität zur Verhinderung von Werkzeugbrüchen und Festigkeit zur Sicherung der Maßhaltigkeit auf ein hohes Niveau einzustellen und ein Verschleiß zu minimieren.To improve the service life of a cold work tool in use with high overall stress, the material properties ductility to prevent tool breakage and strength to ensure dimensional stability are equally set to a high level and to minimize wear.
Erhöhte Beständigkeit gegen abrasiven Verschleiß weisen Eisenbasis-Werkstoffe mit hohem Karbidanteil, insbesondere mit hohem Monokarbidanteil in einer harten Matrix auf. Derartige Stähle besitzen zumeist einen hohen Kohlenstoffgehalt bis 2,5 Gew.-% bei einer Konzentration von monokarbidbildenden Elementen bis 15 Gew.-%, also einen hohen Primär-Karbidanteil, haben jedoch eine geringe Materialzähigkeit im thermisch vergüteten Zustand. Durch eine pulvermetallurgische Herstellung lässt sich die Gefügestruktur, insbesondere die Karbidgröße und die Karbidverteilung im Werkstoff des Gegenstandes verbessern, vielfach kann jedoch eine erforderliche Materialzähigkeit nicht erzielt werden.Increased resistance to abrasive wear is found in iron-based materials with a high carbide content, in particular with a high monocarbide content in a hard matrix. Such steels usually have a high carbon content up to 2.5 wt .-% at a concentration of monocarbide-forming elements to 15 wt .-%, ie a high primary carbide content, but have a low material toughness in the thermally tempered state. Through a powder metallurgical Production, the microstructure, in particular the carbide size and the carbide distribution in the material of the article can be improved, many times, however, a required material toughness can not be achieved.
Verbesserte Zähigkeitseigenschaften können bei typischen hochlegierten Schnellarbeitsstahl-Werkstoffen, zum Beispiel nach DIN Werkstoff No. 1.3351 bei pulvermetallurgischer Fertigung der Teile erzielt werden, jedoch reicht diese Zähigkeitserhöhung des Materials für besonders beanspruchte Gegenstände nicht aus, sodass im Langzeitbetrieb vielfach ein Ausfall durch Bruch derselben erfolgt.Improved toughness properties can be achieved in typical high-alloyed high-speed steel materials, for example according to DIN Werkstoff no. 1.3351 be achieved in powder metallurgical production of the parts, but this toughening of the material for particularly stressed items is not enough, so that in long-term operation often a failure by breaking the same occurs.
Ziel der Erfindung ist nun, einen Kaltarbeitsstahl-Gegenstand zu schaffen, dessen Werkstoff bei hoher Verschleißbeständigkeit und Härte eine erhöhte Zähigkeit sowie eine dergleichen Druckfestigkeit besitzt und eine verbesserte Ermüdungsfestigkeit aufweist. Mit anderen Worten dargelegt: es ist Aufgabe der Erfindung, einen Kaltarbeitsstahl-Gegenstand mit gleichzeitig hohen Festigkeits- und Duktilitäts-Werten zu kennzeichnen, welcher Gegenstand, insbesondere in einer Ausführungsform als Matrizen und Stempel, hohe Wirtschaftlichkeit bei einer Großzahlfertigung von Teilen erbringt.The object of the invention is therefore to provide a cold work tool article whose material, with high wear resistance and hardness, has increased toughness as well as a similar compressive strength and has improved fatigue strength. In other words, it is the object of the invention to characterize a cold work tool steel article with simultaneously high strength and ductility values, which article, especially in one embodiment as dies and punches, provides high economy in a large number of parts.
Dieses Ziel wird erfindungsgemäß bei einem Kaltarbeitsstahl-Gegenstand mit einer chemischen Zusammensetzung des Werkstoffes in Gew.-%:
Die mit der Erfindung erreichten Vorteile bestehen im Wesentlichen darin, dass eine Werkstoffzusammensetzung in engen Grenzen sowie eine pulvermetallurgische Herstellung synergetisch die Voraussetzungen für einen Kaltarbeitsstahl-Gegenstand erstellen, welcher nach einem thermischen Vergüten ein gewünschtes Eigenschaftsprofil aufweist.The advantages achieved with the invention consist essentially in the fact that a material composition within narrow limits as well as a powder metallurgical production synergetically create the conditions for a cold work tool which has a desired property profile after thermal quenching.
In der chemischen Zusammensetzung des Werkstoffes sind die Aktivitäten der Legierungselemente im Hinblick auf eine Gefügeausbildung im vergüteten Zustand und auf geforderte Materialeigenschaften aufeinander wirkungskinetisch abgestimmt.In the chemical composition of the material, the activities of the alloying elements with respect to a microstructure in the quenched state and on required material properties are coordinated with each other kinetic kinetics.
Der Kohlenstoffgehalt ist auf die Summe der Karbidbildner in der Legierung ausgerichtet, um einerseits Karbide zu formen und andererseits die Härtbarkeit und die gewünschten Eigenschaften der Matrix zu bestimmen. Konzentrationen von Kohlenstoff von mehr als 0,6 Gew.-% sind erforderlich, um bei den vorgesehenen Maximalgehalten der karbidbildenden Elemente beim Vergüten hohe Härtewerte der Matrix zu erreichen, hingegen sind Gehalte von geringer als 1,0 Gew.-% wichtig, um eine gewünschte Karbidmenge und Karbidmorphologie einzustellen.The carbon content is aligned with the sum of the carbide formers in the alloy to both form carbides and to determine the hardenability and desired properties of the matrix. Concentrations of carbon of more than 0.6% by weight are required to achieve high hardness values of the matrix at the intended maximum contents of the carbide-forming elements during tempering, whereas contents of less than 1.0% by weight are important in order to obtain a to set the desired amount of carbide and carbide morphology.
Die karbidbildenden Elemente Chrom (Cr), Molybdän (Mo), Vanadin (V) und Wolfram (W) sind legierungstechnisch gemeinsam zu betrachten, weil deren Kohlenstoffaktivität, wie sich zeigte, in Summe die Zusammensetzung des Austenits- bzw. der kubisch-flächenzentrierten Atomstruktur bei Härtetemperatur und in der Folge die Matrixeigenschaften und die sekundären Karbid-Ausscheidungen nach einem mindestens einmaligen Anlassen bestimmen.The carbide-forming elements chromium (Cr), molybdenum (Mo), vanadium (V) and tungsten (W) are to be regarded as alloying together because their carbon activity, as it turned out, totals the composition of the austenite or cubic face-centered atomic structure at curing temperature and subsequently the matrix properties and the secondary Determine carbide precipitations after at least one annealing.
Dabei ist es wichtig, dass der Vanadin-Gehalt der Legierung in Gew.-% größer als 1,0, jedoch geringer als 2,9 ist, um einerseits ausreichend Monokarbide und andererseits genügend Sekundärhärtepotential darzustellen. Das Sekundärhärtepotential muss dabei mit einem Residual-Vanadin und den Gehalten der Elemente Molybdän (Mo) und Wolfram (W) gesehen werden, weil durch Konzentrationen in Gew.-% von 3,8 Molybdän (Mo), sowie 3,4 Wolfram (W) und größer bereits eine Verschlechterung der Matrixzähigkeit verursacht wird, wo hingegen größere Gehalte als 1,9 Molybdän (Mo) und 1,8 Wolfram (W) für eine vorteilhafte Vanadinmaskierung zur Vermeidung großer scharfkantiger Monokarbide erforderlich sind.It is important that the vanadium content of the alloy in wt .-% is greater than 1.0, but less than 2.9, on the one hand to represent sufficient monocarbides and on the other hand enough secondary hardness potential. The secondary hardness potential must be seen with a residual vanadium and the contents of the elements molybdenum (Mo) and tungsten (W), because by concentrations in wt .-% of 3.8 molybdenum (Mo), and 3.4 tungsten (W ) and larger already causes a deterioration of the matrix toughness, whereas larger contents than 1.9 molybdenum (Mo) and 1.8 tungsten (W) are required for an advantageous vanadium masking in order to avoid large sharp-edged monocarbides.
Für diese Wechselwirkung der Elemente kann es auch wichtig sein, dass der Molybdän-Gehalt um höchstens 10% größer ist als jener von Wolfram (W).For this interaction of the elements, it may also be important that the molybdenum content is at most 10% greater than that of tungsten (W).
Für eine Härteannahme und Durchhärtbarkeit des Werkstoffes sind die Elemente Chrom (Cr), Silizium (Si), Mangan (Mn) und in geringem Ausmaß Nickel (Ni) sowie Kobalt (Co) von Bedeutung.The elements chromium (Cr), silicon (Si), manganese (Mn) and, to a lesser extent, nickel (Ni) and cobalt (Co) are important for the hardening and hardenability of the material.
Silizium-Gehalte von mehr als 0,3 Gew.-% sind zur Sicherstellung niedriger Sauerstoffgehalte im Material erforderlich. Weniger als 0,85 Gew.-% Silizium sollen in der Legierung vorgesehen sein, um einer Ferrit-stabilisierenden Wirkung und einer Verringerung der Härteannahme der Matrix durch dieses Element entgegenzuwirken.Silicon contents of more than 0.3% by weight are required to ensure low levels of oxygen in the material. Less than 0.85% by weight of silicon should be included in the alloy to counteract a ferrite stabilizing effect and a reduction in the cure of the matrix by this element.
Mangan als wichtiges, eine erforderliche Abkühlgeschwindigkeit bei der Härtung des Gegenstandes steuerndes Element, soll erfindungsgegemäß Gehalte im Werkstoff in Gew.-% von weniger als 1,5 aufweisen. Weil jedoch auch für eine Bindung Restschwefels in der Legierung geringe Mangankonzentrationen erforderlich sind, ist ein Minimalwert von größer als 0,2 Gew.-% vorzusehen.Manganese as an important, a required cooling rate in the curing of the article controlling element should, according to the invention have contents in the wt .-% of less than 1.5. However, since low manganese concentrations are also required for binding residual sulfur in the alloy, a minimum value of greater than 0.2% by weight must be provided.
Um eine Martensitbildung bei der Abkühlung von einer Härtetemperatur nicht unerwünscht zu beeinflussen, sind Nickelgehalte im Werkstoff von weniger als 0,9 Gew.-% einzustellen.To avoid martensite formation on cooling from a hardening temperature To influence undesirable, nickel contents in the material of less than 0.9 wt .-% can be adjusted.
Kobalt ist zwar auch wirksam im Hinblick auf die anzuwendende Vergütetechnologie, jedoch wurde erfindungsgemäß diese Wirkung legierungstechnisch berücksichtigt. Für einen Erhalt einer hohen Härte durch Mischkristallverfestigung des Werkstoffes ist eine Konzentration in der Matrix von mehr als 3,8 und weniger als 5,8 Gew.-% Kobalt bedeutungsvoll. In den erfindungsgemäßen Grenzen wird durch Kobalt die Kinetik und die Größe von sekundären Karbidausscheidungen günstig im Hinblick auf die Materialeigenschaften beeinflusst. Es werden sehr feine, die Sekundärhärte darstellende Karbide gebildet und deren Vergröberungsneigung verringert, wodurch eine wesentlich verzögerte Entfestigung der vergüteten Legierung durch erhöhte Temperaturen erfolgt. Geringere Kobaltgehalte als 3,8 Gew.-% erniedrigen die Härte sowie die Dauerstandsfestigkeit des Materials. Kobaltwerte von 5,8 Gew.-% und höher vermindern wiederum besonders die Zähigkeit des Werkstoffes.Although cobalt is also effective with regard to the applicable tempering technology, according to the invention, this effect has been taken into account by alloying technology. To obtain a high hardness by solid solution strengthening of the material, a concentration in the matrix of more than 3.8 and less than 5.8 wt% of cobalt is meaningful. In the limits according to the invention, the kinetics and the size of secondary carbide precipitates are favorably influenced by cobalt with regard to the material properties. Very fine carbides representing the secondary hardness are formed and their coarsening tendency is reduced, whereby a significantly delayed softening of the quenched alloy by elevated temperatures takes place. Lower cobalt contents than 3.8% by weight lower the hardness and the fatigue strength of the material. Cobalt values of 5.8% by weight and higher, in turn, particularly reduce the toughness of the material.
Es ist bekannt, dass Aluminium teilweise als Substitutionselement für Kobalt fungieren kann und bei Schnellarbeitsstählen die Schneidleistung erhöht. Auf Grund einer Nitridbildungsneigung sowie einer einfachen Verdüsungstechnologie und einer niedrigen Stickstoffkonzentration im Metall von geringer als 0,2 Gew.-% wegen sollte der Aluminiumgehalt in der Legierung weniger als 0,045 Gew.-% betragen.It is known that aluminum can partially act as a substitution element for cobalt and increases the cutting performance of high speed steels. Due to a nitriding tendency as well as a simple atomization technology and a low nitrogen concentration in the metal of less than 0.2 wt%, the aluminum content in the alloy should be less than 0.045 wt%.
Sauerstoffkonzentrationen von größer als 0,012 Gew.-% erniedrigen, wie gefunden wurde, auch bei PM-Erzeugung die mechanischen Eigenschaften des erfindungsgemäß zusammengesetzten Werkstoffes.Lower oxygen concentrations of greater than 0.012 wt .-%, as was found, even in PM production, the mechanical properties of the composite material according to the invention.
Durch Phosphorgehalte von über 0,03 Gew.-% wird die Herstellbarkeit verschlechtert.By phosphorus contents of over 0.03 wt .-%, the manufacturability is deteriorated.
Für ein Erreichen von besonders vorteilhaften mechanischen Materialeigenschaften, insbesondere von hoher Festigkeit und Duktilität ist erfindungsgemäß eine pulvermetallurgischen Herstellung des Kaltarbeitsstahl-Gegenstandes wichtig. Durch eine legierungstechnisch bewirkte Ausformung von im Wesentlichen runden primären Karbiden mit geringem Durchmesser und einem hohen Reinheitsgrad bei günstiger Gefügeausbildung des Werkstoffes war es möglich, eine üblicherweise von scharfkantigen Karbid- und Verunreinigungspartikeln ausgelöste Rissinitiation zu vermeiden. Derart ist bei hoher Materialhärte eine hohe Schlagbiegearbeit des Werkstoffes sowie eine günstige Ermüdungsfestigkeit des Stahl- Gegenstandes im Einsatz erreichbar.For achieving particularly advantageous mechanical material properties, in particular of high strength and ductility, powder-metallurgical production of the cold-work tool article is important in accordance with the invention. Due to an alloying effect caused by im Essentially round primary carbides with a small diameter and a high degree of purity with favorable microstructural formation of the material, it was possible to avoid a crack initiation usually caused by sharp-edged carbide and contaminant particles. In this way, with high material hardness, a high impact bending work of the material as well as a favorable fatigue strength of the steel object can be achieved in use.
Die Gebrauchseigenschaften eines Kaltarbeitsstahl-Gegenstandes nach der Erfindung können weiter gesteigert werden, wenn ein oder mehrere Element(e) im Werkstoff in einer Konzentration in Gew.-% vorliegen von:
Von besonderem Vorteil für hohe Zähigkeitswerte und gute Dauerstandseigenschaften des Gegenstandes ist, wenn ein oder mehrere Verunreinigungselement(e) im Werkstoff eine Konzentration in Gew.-% aufweisen von:
Die Reinheit und somit auch die mechanischen Eigenschaften des Materials, insbesondere die Zähigkeit, können gefördert werden, wenn das pulvermetallurgische Verfahren ein Verdüsen der Schmelze mit hochreinem Stickstoff zu Metallpulver mit einer Pulverkorngröße von höchstens 500 µm und in der Folge im Wesentlichen ein Einbringen des Pulvers unter Vermeidung von Sauerstoffzutritt in ein Gefäß und ein heißisostatisches Pressen des Metallpulvers im verschlossenen Gefäß zur Erstellung eines Rohlings umfasst.The purity and thus also the mechanical properties of the material, in particular the toughness, can be promoted if the powder metallurgy process atomizing the melt with high-purity nitrogen to metal powder having a powder grain size of at most 500 microns and subsequently substantially introducing the powder Prevention of oxygen access into a vessel and a hot isostatic pressing of the metal powder in the closed vessel to create a blank comprises.
Für eine wirtschaftliche Fertigung eines Kaltarbeitsstahl-Gegenstandes, aber auch der Materialeigenschaften wegen, kann es günstig sein, wenn der heißisostatisch gepresste Rohling durch Warmumformung weiterverarbeitet ist.For an economical production of a cold work tool article, but also because of the material properties, it may be favorable if the hot isostatically pressed blank is further processed by hot forming.
Wenn, wie vorgesehen sein kann, der Kaltarbeitsstahl-Gegenstand eine Druckfließgrenze von mehr als 2700 MPa, gemessen bei einer Härte von 61 HRC besitzt, sind höchst zuverlässige Fließpressmatrizen mit komplizierten feingliedrigen Formteilen herstellbar, welche auch im Langzeitbetrieb geringe Abnützung der Oberfläche und dergleichen Rissgefahr zeigen.If, as may be provided, the cold work tool article has a pressure flow limit of more than 2700 MPa, measured at a hardness of 61 HRC, highly reliable extrusion dies with complex, delicate moldings can be produced, which exhibit low surface wear and the risk of cracking even in long-term operation ,
Von Vorteil für einen harten Prägeeinsatz mit stoßartiger Belastung im Langzeitbetrieb kann nach der Erfindung vorgesehen sein, dass der Kaltarbeitsstahl-Gegenstand nach einem thermischen Vergüten auf eine Härte von 64 HRC eine Schlagbiegearbeit bei Raumtemperatur von größer 80,0 Joule (J), vorzugsweise von größer 100 Joule (J), besitzt.Of advantage for a hard embossing insert with shock-like load in long-term operation can be provided according to the invention that the cold work tool steel after thermal quenching to a hardness of 64 HRC an impact work at room temperature of greater than 80.0 Joule (J), preferably larger 100 joules (J), owns.
Im Folgenden soll die Erfindung anhand von wissenschaftlichen Erprobungen sowie Erprobungsergebnissen im Vergleich und Schlußfolgerungen erläutert werden.In the following, the invention will be explained on the basis of scientific tests and test results in comparison and conclusions.
Zur Kennzeichnung des erfindungsgemäßen Gegenstandes wurde die Schlagbiegearbeit bei Raumtemperatur gemäß DIN 51222 von ungekerbten Proben 7 x 10 x 55 mm herangezogen, weil derartige Werte die genaue Beurteilung des Zähigkeitsverhaltens ermöglichen.To characterize the article according to the invention, the impact bending work at room temperature according to DIN 51222 of unnotched samples 7 x 10 x 55 mm was used, because such values allow the accurate assessment of the toughness behavior.
Für eine Ermittlung der Bruchdehnung und der plastischen Arbeit aus dem statischen einachsigen Zugversuch wurden Sonderzugproben mit im Durchmesser verlaufend vergrößerten Einspannköpfen in Kugelform verwendet, wobei die Einspannvorrichtung in der Prüfmaschine der Kugelkopfgeometrie Rechnung trug. Derartige Untersuchungen sind in der Literatur (6th Intemational Tooling Conference, The Use of Tool Steels: Experience and Research, Karlstad University 10 - 13 September 2002 , Material Behaviour of Powder- Metallurgically Processed Tool Steels in Tensile and Bending Tests, Seite 169 -178) beschrieben.For a determination of the elongation at break and the plastic work from the static uniaxial tensile test, special tensile specimens with diameter-increasing enlarged clamping heads in spherical form were used, whereby the clamping device in the testing machine took into account the ball head geometry. Such investigations are reported in the literature (6th Intemational Tooling Conference, The Use of Tool Steels: Experience and Research, Karlstad University 10-13 September 2002, Material Behavior of Powder-Metallurgically Processed Tool Steels in Tensile and Bending Tests, pages 169-178). described.
Die 0,2 % Stauchgrenze des Werkstoffes wurde im Druckversuch nach DIN 50106 bei Raumtemperatur ermittelt.The 0.2% compression limit of the material was determined in a pressure test according to DIN 50106 at room temperature.
Eine Prüfung des Abrasionsverschleißes erfolgte mit SiC- Schleifpapier P 120.Abrasion wear was tested with SiC abrasive paper P 120.
Die Werkstoffprüfung verwendet unterschiedliche Methoden zur Charakterisierung von Festigkeit und Duktilität von metallischen Werkstoffen. Der wichtigste Versuch ist der einachsige Zugversuch. Mit diesem Versuch können wesentliche Festigkeits- und Duktilitätskennwerte bestimmt werden. Darüber hinaus erlaubt dieser Versuch Aussagen über das Verfestigungsverhalten der Werkstoffe unter einachsiger Zugbeanspruchung.Materials testing uses different methods to characterize the strength and ductility of metallic materials. The most important experiment is the uniaxial tensile test. With this test, essential strength and ductility characteristics can be determined. In addition, this experiment allows statements about the solidification behavior of the materials under uniaxial Tensile stress.
In Fig. 1 ist die Bruchdehnung des erfindungsgemäßen Werkstoffes im Vergleich mit einem Schnellstahl HS-6-5-4 in Abhängigkeit von einer mit einer thermischen Vergütung eingestellten Materialhärte dargestellt, wobei die Prüfung unter Verwendung der oben beschriebenen Proben erfolgte.In Fig. 1, the elongation at break of the material according to the invention in comparison with a HS-6-5-4 high speed steel is shown as a function of a set with a thermal hardness material hardness, wherein the test was carried out using the samples described above.
Die Bruchdehnung der erfindungsgemäßen Legierung liegt im gesamten Härtebereich der Werkstoffe höher als diejenige des Vergleichsstahles und weist insbesondere im oberen Härtebereich von 58 HRC bis 62 HRC eine bis 4mal höhere Bruchdehnung auf.The elongation at break of the alloy according to the invention is higher than that of the comparative steel in the entire hardness range of the materials and, in particular in the upper hardness range from 58 HRC to 62 HRC, has an elongation at break 4 times higher.
Die gegenüber dem Stand der Technik vorteilhafte Eigenschaftskombination von hoher Festigkeit und hoher Duktilität des erfindungsgemäßen Werkstoffes zeigt sich im Vergleich der plastischen Arbeit, welche aus dem statischen einachsigen Zugversuch ermittelt wird, besonders signifikant. Bei im Wesentlichen gleichem Anlaßzustand wurde am Werkstoff gemäß der Erfindung bei Raumtemperatur eine um etwa 20% höhere plastische Arbeit im Zugversuch bei einer Materialhärte von 63 HRC ermittelt. Bei einer Materialhärte von 61,5 HRC wurde eine Steigerung der plastischen Arbeit um etwa 50% festgestellt, wobei als Vergleichsmaterial die pulvermetallurgisch hergestellten Schnellarbeitsstähle HS-10-2-5-8-PM und HS-6-5-3-PM herangezogen wurden.The property combination of high strength and high ductility of the material according to the invention, which is advantageous over the prior art, is particularly significant in comparison with the plastic work which is determined from the static uniaxial tensile test. At substantially the same temper, the material according to the invention at room temperature was determined to be about 20% higher plastic work in the tensile test at a material hardness of 63 HRC. With a material hardness of 61.5 HRC, an increase in plastic work of about 50% was found, using the powder-metallurgically produced high-speed steels HS-10-2-5-8-PM and HS-6-5-3-PM as reference material ,
Neben der herausragenden Eigenschaftskombination von Festigkeit und Duktilität, welche oben gezeigt wurde, verfügt die erfindungsgemäße Legierung über eine sehr gute abrasive Verschleißfestigkeit, welche im SiC-Schleifpapiertest ermittelt wurde. Diese Eigenschaft wurde trotz eines gegenüber in diesem Anwendungsfeld verwendeten Standard-PM-Legierungen verminderten Primärkarbidgehaltes erzielt.In addition to the outstanding property combination of strength and ductility shown above, the alloy according to the invention has a very good abrasive wear resistance, which was determined in the SiC abrasive paper test. This property was achieved despite a reduced primary carbide content compared to standard PM alloys used in this field of application.
Der mittlere Verschleißwert beträgt für die angegebenen Legierungen einen Wert von 7g-1bei einer Härte von 61 HRC.The mean wear value for the specified alloys is 7g -1 at a hardness of 61 HRC.
Claims (6)
- Thermally hardened cold-worked steel object comprising a chemical composition of the material in % by weight of:
carbon (C) more than 0.6 and less than 1.0 silicon (Si) more than 0.3 and less than 0.85 manganese (Mn) more than 0.2 and less than 1.5 phosphorus (P) 0.03 in maximum sulphur (S) less than 0.5 chromium (Cr) more than 4.0 and less than 6.2 molybdenum (Mo) more than 1.9 and less than 3.8 nickel (Ni) less than 0.9 vanadium (V) more than 1.0 and less than 2.9 tungsten (W) more than 1.8 and less than 3.4 copper (Cu) less than 0.7 cobalt (Co) more than 3.8 and less than 5.8 aluminium (Al) less than 0.045 nitrogen (N) less than 0.2 oxygen (O) 0.012 in maximum, and optionally tin (Sn) 0.02 in maximum antimony (Sb) 0.022 in maximum arsenic (As) 0.03 in maximum selenium (Se) 0.012 in maximum bismuth (Bi) 0.01 in maximum,
as well as smelting conditioned accompanying and impurity elements, the material being produced according to a powder metallurgical process and has, after thermal hardening up to a hardness of 64 HRC, an impact flexure energy at ambient temperature of more than 40.0 Joule (J). - Cold-worked steel object according to claim 1, wherein one or more element(s) in the material is (are) present in a concentration in % by weight of:
carbon (C) more than 0.75 and less than 0.94 particularly more than 0.8 and less than 0.9 silicon (Si) more than 0.35 and less than 0.7 particularly more than 0.4 and less than 0.65 manganese (Mn) more than 0.25 and less than 0.9 particularly more than 0.3 and less than 0.5 phosphorus (P) 0.025 in maximum sulphur (S) less than 0.34 particularly 0.025 in maximum chromium (Cr) more than 0.4 and less than 5.9 particularly more than 4.1 and less than 4.5 molybdenum (Mo) more than 2.2 and less than 3.4 particularly more than 2.5 and less than 3.0 nickel (Ni) less than 0.5 vanadium (V) more than 1.5 and less than 2.6 particularly more than 1.8 and less than 2.4 tungsten (W) more than 2.0 and less than 3.0 copper (Cu) less than 0.45 particularly 0.3 in maximum aluminium (Al) less than 0.065 particularly more than 0.01 and less than 0.05 nitrogen (N) more than 0.01 and less than 0.1 particularly more than 0.05 and less than 0.08 oxygen (O) 0.01 in maximum particularly 0.009 in maximum. - Cold-worked steel object according to claim 1 or 2, wherein the metallurgical process comprises atomising the melt with nitrogen to a metal powder having a powder grain size of 500 µm in maximum, and subsequently substantially introducing the powder, while avoiding the access of oxygen, into a receptacle, and high-temperature isostatic compressing the metal powder in the closed receptacle to produce a blank.
- Cold-worked steel object according to any of claims 1 to 3, wherein the high-temperature isostatically compressed blank is further processed by hot deformation.
- Cold-worked steel object according to any of claims 1 to 4, which has a pressure yield point of more than 2700 MPa, when measured at a hardness of 61 HRC.
- Cold-worked steel object according to any of claims 1 to 5, which has an impact flexure energy at ambient temperature of more than 80.0 Joule (J), preferably more than 100 Joule (J).
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PL04450082T PL1471160T3 (en) | 2003-04-24 | 2004-04-01 | Cold-worked Steel Object |
| AT04450082T ATE340878T1 (en) | 2003-04-24 | 2004-04-01 | COLD WORK STEEL ITEM |
| SI200430119T SI1471160T1 (en) | 2003-04-24 | 2004-04-01 | Cold-worked Steel Object |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| AT0062703A AT412000B (en) | 2003-04-24 | 2003-04-24 | Cold-worked steel with greater strength and increased ductility, used for, e.g., pressing tools and forgings, has specified composition |
| AT6272003 | 2003-04-24 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP1471160A1 EP1471160A1 (en) | 2004-10-27 |
| EP1471160B1 true EP1471160B1 (en) | 2006-09-27 |
Family
ID=30120896
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP04450082A Expired - Lifetime EP1471160B1 (en) | 2003-04-24 | 2004-04-01 | Cold-worked Steel Object |
Country Status (15)
| Country | Link |
|---|---|
| US (1) | US7682417B2 (en) |
| EP (1) | EP1471160B1 (en) |
| AR (1) | AR044020A1 (en) |
| AT (2) | AT412000B (en) |
| BR (1) | BRPI0401477B1 (en) |
| CA (1) | CA2465146C (en) |
| DE (1) | DE502004001560D1 (en) |
| DK (1) | DK1471160T3 (en) |
| ES (1) | ES2274414T3 (en) |
| HR (1) | HRP20060447T3 (en) |
| PL (1) | PL1471160T3 (en) |
| PT (1) | PT1471160E (en) |
| RU (1) | RU2270879C2 (en) |
| SI (1) | SI1471160T1 (en) |
| UA (1) | UA81396C2 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AT508591B1 (en) * | 2009-03-12 | 2011-04-15 | Boehler Edelstahl Gmbh & Co Kg | COLD WORK STEEL OBJECT |
| CN106191695A (en) * | 2016-07-10 | 2016-12-07 | 程叙毅 | A kind of antiwear heat resisting alloy material and preparation method |
| CN105925898A (en) * | 2016-07-10 | 2016-09-07 | 程叙毅 | Intake valve seat ring material and preparing method |
| CN106191668A (en) * | 2016-07-10 | 2016-12-07 | 程叙毅 | A kind of exhaust valve seat loop material and preparation method |
| DE102021101105A1 (en) | 2021-01-20 | 2022-07-21 | Voestalpine Böhler Edelstahl Gmbh & Co Kg | Process for producing a tool steel as a carrier for PVD coatings and a tool steel |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62250158A (en) * | 1986-04-24 | 1987-10-31 | Sumitomo Metal Ind Ltd | Steel for hot forging die |
| JP2960496B2 (en) * | 1989-12-12 | 1999-10-06 | 日立金属株式会社 | Cold tool steel |
| JPH04180541A (en) * | 1990-11-14 | 1992-06-26 | Hitachi Metals Ltd | Cold-working tool steel excellent in machinability |
| JP2711788B2 (en) * | 1993-02-25 | 1998-02-10 | 山陽特殊製鋼株式会社 | Manufacturing method of large dies for extrusion of light metals |
| US5522914A (en) * | 1993-09-27 | 1996-06-04 | Crucible Materials Corporation | Sulfur-containing powder-metallurgy tool steel article |
| CA2131652C (en) * | 1993-09-27 | 2004-06-01 | William Stasko | Sulfur-containing powder-metallurgy tool steel article |
| JPH07316739A (en) * | 1994-05-20 | 1995-12-05 | Daido Steel Co Ltd | Cold tool steel |
| JP2636816B2 (en) * | 1995-09-08 | 1997-07-30 | 大同特殊鋼株式会社 | Alloy tool steel |
| JP3517505B2 (en) * | 1996-01-16 | 2004-04-12 | 日立粉末冶金株式会社 | Raw material powder for sintered wear resistant material |
| AT409389B (en) * | 2001-04-11 | 2002-07-25 | Boehler Edelstahl | PM high-speed steel with a high resistance to heat |
| JP4281857B2 (en) * | 2001-08-09 | 2009-06-17 | 株式会社不二越 | Sintered tool steel and manufacturing method thereof |
-
2003
- 2003-04-24 AT AT0062703A patent/AT412000B/en not_active IP Right Cessation
-
2004
- 2004-03-16 UA UA2004031961A patent/UA81396C2/en unknown
- 2004-04-01 DE DE502004001560T patent/DE502004001560D1/en not_active Expired - Lifetime
- 2004-04-01 SI SI200430119T patent/SI1471160T1/en unknown
- 2004-04-01 ES ES04450082T patent/ES2274414T3/en not_active Expired - Lifetime
- 2004-04-01 DK DK04450082T patent/DK1471160T3/en active
- 2004-04-01 PL PL04450082T patent/PL1471160T3/en unknown
- 2004-04-01 PT PT04450082T patent/PT1471160E/en unknown
- 2004-04-01 AT AT04450082T patent/ATE340878T1/en active
- 2004-04-01 EP EP04450082A patent/EP1471160B1/en not_active Expired - Lifetime
- 2004-04-15 AR ARP040101267A patent/AR044020A1/en active IP Right Grant
- 2004-04-22 BR BRPI0401477-4A patent/BRPI0401477B1/en active IP Right Grant
- 2004-04-23 RU RU2004112557/02A patent/RU2270879C2/en active
- 2004-04-23 US US10/830,003 patent/US7682417B2/en active Active
- 2004-04-23 CA CA002465146A patent/CA2465146C/en not_active Expired - Lifetime
-
2006
- 2006-12-19 HR HR20060447T patent/HRP20060447T3/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| PT1471160E (en) | 2007-01-31 |
| ES2274414T3 (en) | 2007-05-16 |
| US20050002819A1 (en) | 2005-01-06 |
| ATE340878T1 (en) | 2006-10-15 |
| EP1471160A1 (en) | 2004-10-27 |
| AR044020A1 (en) | 2005-08-24 |
| SI1471160T1 (en) | 2007-02-28 |
| US7682417B2 (en) | 2010-03-23 |
| DE502004001560D1 (en) | 2006-11-09 |
| CA2465146A1 (en) | 2004-10-24 |
| PL1471160T3 (en) | 2007-02-28 |
| RU2270879C2 (en) | 2006-02-27 |
| UA81396C2 (en) | 2008-01-10 |
| BRPI0401477B1 (en) | 2013-05-28 |
| HRP20060447T3 (en) | 2007-03-31 |
| DK1471160T3 (en) | 2007-01-29 |
| RU2004112557A (en) | 2005-10-27 |
| AT412000B (en) | 2004-08-26 |
| CA2465146C (en) | 2008-04-08 |
| ATA6272003A (en) | 2004-01-15 |
| BRPI0401477A (en) | 2005-01-18 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP3228724B1 (en) | Tool steel, in particular hot-work steel, and steel object | |
| AT507215B1 (en) | WEAR-RESISTANT MATERIAL | |
| DE69818138T2 (en) | Cold work tool steel particles with high impact strength from metal powder and process for its production | |
| EP1249511B1 (en) | High speed steel with good high temperature strength manufactured by powder metallurgy | |
| DE3041565C2 (en) | ||
| EP3323902B1 (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 | |
| AT410447B (en) | HOT STEEL SUBJECT | |
| EP0348380B1 (en) | Use of an iron-base alloy in the manufacture of sintered parts with a high corrosion resistance, a high wear resistance as well as a high toughness and compression strength, especially for use in the processing of synthetic materials | |
| DE102019135830A1 (en) | Method of making a hot work steel article | |
| WO2001079575A1 (en) | Nitrogen alloyed steel, spray compacted steel, method for the production thereof and composite material produced from said steel | |
| EP1647606B1 (en) | High hardness and wear resistant nickel based alloy for use as high temperature tooling | |
| EP1471160B1 (en) | Cold-worked Steel Object | |
| WO2021032893A1 (en) | Tool steel for cold-working and high-speed applications | |
| 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 | |
| DE60126646T2 (en) | STEEL ALLOY, HOLDER AND BRACKET PARTS FOR PLASTIC TOOLS AND GUARANTEED COVERS FOR HOLDER AND HOLDER PARTS | |
| EP0733719B1 (en) | Iron base alloy for use at high temperature | |
| EP2233596B1 (en) | Cold worked steel object | |
| EP1052304A1 (en) | Martensitic corrosion resistant chromium steel | |
| DE102021101105A1 (en) | Process for producing a tool steel as a carrier for PVD coatings and a tool steel | |
| DE4334062A1 (en) | Tool steel compsn. having high temp. strength - comprises manganese@, chromium@, molybdenum@, tungsten@, vanadium@, cobalt@ and nitrogen@ | |
| EP1785500A1 (en) | A wear and corrosion resistant highly alloyed steel powder |
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 IT LI LU MC NL PL PT RO SE SI SK TR |
|
| AX | Request for extension of the european patent |
Extension state: AL HR LT LV MK |
|
| 17P | Request for examination filed |
Effective date: 20050103 |
|
| 17Q | First examination report despatched |
Effective date: 20050210 |
|
| AKX | Designation fees paid |
Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PL PT RO SE SI SK TR |
|
| AXX | Extension fees paid |
Extension state: HR Payment date: 20050103 |
|
| REG | Reference to a national code |
Ref country code: HK Ref legal event code: DE Ref document number: 1072783 Country of ref document: HK |
|
| GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
| 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 IT LI LU MC NL PL PT RO SE SI SK TR |
|
| AX | Request for extension of the european patent |
Extension state: HR |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED. Effective date: 20060927 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: 20060927 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: 20060927 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: 20060927 |
|
| 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: 502004001560 Country of ref document: DE Date of ref document: 20061109 Kind code of ref document: P |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: TUEP Ref document number: P20060447 Country of ref document: HR |
|
| 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: 20061227 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: NV Representative=s name: HANS RUDOLF GACHNANG PATENTANWALT |
|
| 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: 20061219 |
|
| REG | Reference to a national code |
Ref country code: DK Ref legal event code: T3 |
|
| REG | Reference to a national code |
Ref country code: PT Ref legal event code: SC4A Free format text: AVAILABILITY OF NATIONAL TRANSLATION Effective date: 20061227 |
|
| REG | Reference to a national code |
Ref country code: PL Ref legal event code: T3 Ref country code: HU Ref legal event code: AG4A Ref document number: E001047 Country of ref document: HU |
|
| REG | Reference to a national code |
Ref country code: HK Ref legal event code: GR Ref document number: 1072783 Country of ref document: HK |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: T1PR Ref document number: P20060447 Country of ref document: HR |
|
| REG | Reference to a national code |
Ref country code: IE Ref legal event code: FD4D |
|
| ET | Fr: translation filed | ||
| REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2274414 Country of ref document: ES Kind code of ref document: T3 |
|
| 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: 20070628 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20061228 |
|
| 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: 20060927 |
|
| PGRI | Patent reinstated in contracting state [announced from national office to epo] |
Ref country code: IT Effective date: 20080601 |
|
| 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: 20070430 |
|
| 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: 20060927 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: NV Representative=s name: GACHNANG AG PATENTANWAELTE, CH |
|
| 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: FR Ref legal event code: PLFP Year of fee payment: 14 |
|
| REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 15 |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20060447 Country of ref document: HR Payment date: 20190321 Year of fee payment: 16 |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20060447 Country of ref document: HR Payment date: 20200320 Year of fee payment: 17 |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20060447 Country of ref document: HR Payment date: 20210319 Year of fee payment: 18 |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20060447 Country of ref document: HR Payment date: 20220318 Year of fee payment: 19 |
|
| REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20060447 Country of ref document: HR Payment date: 20230320 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20230322 Year of fee payment: 20 Ref country code: SK Payment date: 20230320 Year of fee payment: 20 Ref country code: PT Payment date: 20230319 Year of fee payment: 20 Ref country code: PL Payment date: 20230321 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20230426 Year of fee payment: 20 Ref country code: LU Payment date: 20230427 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IT Payment date: 20230419 Year of fee payment: 20 Ref country code: FR Payment date: 20230425 Year of fee payment: 20 Ref country code: ES Payment date: 20230503 Year of fee payment: 20 Ref country code: DK Payment date: 20230427 Year of fee payment: 20 Ref country code: DE Payment date: 20230427 Year of fee payment: 20 Ref country code: CH Payment date: 20230502 Year of fee payment: 20 |
|
| 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: SI Payment date: 20230321 Year of fee payment: 20 Ref country code: SE Payment date: 20230427 Year of fee payment: 20 Ref country code: HU Payment date: 20230331 Year of fee payment: 20 Ref country code: FI Payment date: 20230425 Year of fee payment: 20 Ref country code: AT Payment date: 20230321 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20230427 Year of fee payment: 20 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20230427 Year of fee payment: 20 |
|
| REG | Reference to a national code |
Ref country code: DE Ref legal event code: R071 Ref document number: 502004001560 Country of ref document: DE |
|
| REG | Reference to a national code |
Ref country code: NL Ref legal event code: MK Effective date: 20240331 |
|
| REG | Reference to a national code |
Ref country code: DK Ref legal event code: EUP Expiry date: 20240401 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |