EP1249510A2 - Verfahren zur pulvermetallurgischen Herstellung von Gegenständen aus Werkzeugstahl - Google Patents
Verfahren zur pulvermetallurgischen Herstellung von Gegenständen aus Werkzeugstahl Download PDFInfo
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- EP1249510A2 EP1249510A2 EP01890158A EP01890158A EP1249510A2 EP 1249510 A2 EP1249510 A2 EP 1249510A2 EP 01890158 A EP01890158 A EP 01890158A EP 01890158 A EP01890158 A EP 01890158A EP 1249510 A2 EP1249510 A2 EP 1249510A2
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- powder
- melt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- 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
-
- 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
-
- 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
- C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0848—Melting process before atomisation
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0848—Melting process before atomisation
- B22F2009/0852—Electroslag melting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0896—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid particle transport, separation: process and apparatus
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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- 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
- C21D2241/00—Treatments in a special environment
- C21D2241/01—Treatments in a special environment under pressure
- C21D2241/02—Hot isostatic pressing
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- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
Definitions
- the invention relates to a method for powder metallurgical production of tool steel objects with improved homogeneity, higher Purity and improved properties.
- the invention relates to a tool steel object improved property profile.
- Tool steels with high carbon concentrations and high contents carbide-forming elements are used for cutting parts and components with high Wear resistance used. Because now when such alloys solidify in molds inhomogeneities as well as rough primary and eutectic carbides are formed, the manufacturing problems and poor mechanical properties of the tools or components created from it is one powder metallurgical production of such parts advantageous.
- a powder metallurgical production essentially involves atomizing one Tool steel melt to metal powder, an introduction and compression of the Metal powder in a container or capsule, closing the capsule and heating and hot isostatic pressing of the powder in the capsule into one dense homogeneous material.
- the invention seeks to remedy this and aims to remedy the lack of quality Articles made of PM tool steel according to the prior art to eliminate and to specify a method of the type mentioned above with which is an isostatically pressed metal body with the highest material isotropy and lowest content of oxidic inclusions can be produced.
- the invention further aims at a tool steel object with improved Processing and usage properties with increased service life.
- This goal is achieved in a generic method in that a Melt is introduced into a metallurgical vessel and conditioned in it, this is an improvement in the oxide purity of the same and an adjustment the temperature to a value above the formation temperature of Primary excretions in the alloy, after which at essentially constant held temperature from this melt by atomization with nitrogen Powder made with an average grain diameter of 50 to 70 microns, in Nitrogen stream disintegrated and while maintaining the nitrogen atmosphere classifies the powder with a maximum grain diameter of 500 ⁇ m, collected, mixed, in a container with a diameter or a thickness of greater than 300 mm and a length of greater than 1000 mm, by mechanical impacts are compressed in this and the container is sealed gas-tight is what then in a hot isostatic press cycle for this the parameters such can be set so that the temperature and pressure increase during the warm-up process be, all-round in the powder body of the container or capsule Pressure of at least 1 to 40 MPa is effective, and then an isostatic Pressing process at a temperature of at least 1100 ° C
- the advantages achieved with the method according to the invention are essentially is based on the fact that synergetically initially through metallurgical work on one in one metallurgical vessel introduced melt their oxidic purity significantly improved and their temperature homogeneous to an advantageous Overheating value can be set, after which atomization of the liquid metal is carried out in such a way that the mean grain diameter is 50 to 70 ⁇ m.
- An inventive distribution of the grain diameter with an average in The range of 50 to 70 ⁇ m enables an unexpectedly high one to be reached Powder density in the capsule, so that on the one hand its shrinkage when hot isostatic presses is low and on the other hand largely complete Isotropy of the pressed dense metal body is present. These benefits too for container sizes with a diameter or a thickness of more than 300 mm and a length of more than 1000 mm.
- the parameters for the hot isostatic press cycle include warming up the Powder in the container with substantially the same increase in temperature and Pressure, which has already been shown to increase the Material density and homogeneity can be achieved.
- the subsequent pressing process takes place in the temperature range from 1100 ° C to 1180 ° C at a pressure of 90 MPa and larger with a duration of at least three hours, followed by one slow cooling of the compact. Press temperatures lower than 1100 ° C and pressures below 90 MPa and press times less than three hours Impact in the material
- the pressed body After the HIP, the pressed body has a completely dense material structure, can be turned into a tool in this condition or after hot forming are processed.
- Powder-metallurgically manufactured tool steel object is its low inclusion content and characteristic of the small inclusion size.
- the high degree of oxide purity which with a K0 value according to DIN 50 602 of im essentially 3 is documented, not only leads to greatly improved mechanical properties, especially at elevated operating temperatures, the Material in all directions. but also improves it Performance characteristics, preferably the edge retention of Fine-cutting tools, to a large extent.
- a particularly striking increase in the quality of the article is achieved in its manufacture by the process according to the invention if the melt is composed of an iron-based alloy and contains% by weight.
- the above chemical composition of the tool steel contains particularly carbide-rich tool steels with high abrasion resistance and high cutting edge retention of the tools made from them. Since high carbide fractions generally impair the mechanical properties of the material, their fundamental improvement by the process according to the invention is of particular importance. It has been shown that these high mechanical characteristics, in particular that of the impact strength of the material, are synergistically due to the small mean grain diameter of the powder, a homogeneous dense filling of the same in the capsule and the high oxidic purity with an isotropic structure of the hot isostatically pressed object ,
- the oxidic degree of purity of the liquid metal can be determined by a metallurgical Work can be effectively improved if the melt is conditioned in the metallurgical vessel with an induced turbulent flow of the same and when the metal bath is completely covered by liquid slag, which is heated in particular by means of direct current passage for a period of time of at least 15 minutes.
- a levy of Oxygen compounds or oxides from the melt and an uptake the same is conveyed into the hot slag, the induced flow of the Metal bath increases efficiency.
- a flow of is known per se Liquid metal in a metallurgical vessel by introducing argon purge gas by at least one gas-permeable sink arranged at the bottom to reach.
- a Compliance with the melt flow diameter and the high kinetic energy of the Gas loading of the metal stream causes a favorable grain distribution and a desired fineness of the metal powder created.
- the conditioning and the Setting the temperature of the liquid metal in the metallurgical vessel as well the high purity of the atomizing gas nitrogen is also the cause for a surprisingly high degree of purity or a low oxygen content of the powder and as a result of the hot isostatically pressed block.
- the soaking time can on the one hand Shortened due to increased heat conduction and the powder mass in view pre-compressed to a largely complete isotropy of the block.
- the further object of the invention to create a tool steel object with improved machining and usage properties with increased service life is achieved in a powder-metallurgically manufactured object made of tool steel with improved material properties consisting of an iron-based alloy containing% by weight.
- Tool steels have a wide range of concentration of each Alloy elements, whereby these always interact and with regard can be seen on the carbon content. Carbon levels less than 0.52 % By weight lead to a low carbide content and / or to a low one Matrix hardness in the heat-treated condition of the steel, whereas higher Content as 3.74 wt .-% carbon, even in a powder metallurgical Manufacturing, the material for use as a tool due to the largely exclude mechanical property profile.
- the high affinity for carbon of the elements Mo, V, Nb / Ta and W results in the desired proportions in a desired carbide and mixed carbide formation in an alloy matrix.
- concentration values in% by weight should be 10.0; 14.9; 2.0; 20.0 must not be exceeded because, on the one hand, this means that the desired remuneration behavior and, on the other hand, the manufacturability and the intended mechanical properties of the materials cannot be achieved.
- Ni can optionally be present in the alloy up to a content of 1.0% by weight without any adverse effect
- Co increases the hot hardness and cutting edge stability of the tools, but has a property-worsening effect from a content of 20.8% by weight.
- Sulfur contents of up to 0.5% by weight improve the machinability of the tool steel without, however, adversely affecting the degree of purity thereof. that the mechanical material values are reduced.
- the tool steel has one defined according to DIN 50 602 K0 value of essentially at most 3.
- DIN 50 602 K0 value essentially at most 3.
- This high degree of purity of the Material not only brings about a great improvement in mechanical Properties in the tempered state, for example a significantly increased Toughness of the material, but it's also the usage properties, especially the edge retention of fine-cut tools for hard Objects raised suddenly.
- This increase in quality of the invention Items made of tool steel made by powder metallurgy is as found was justified in particular by the fact that the small proportion of smaller and Lack of larger non-metallic inclusions one caused by them Crack initiation minimized.
- the powder was introduced from the collecting container into a container or a capsule made of unalloyed steel, whereby by shaking or tapping the same or a compression of the powder filling and subsequently one Closing the capsule were made.
- the one with condensed Alloy powder filled capsule with a diameter of 420 mm ⁇ and one Length of 2000 mm was introduced into the HIP system when cold, after which the pressure and temperature were increased at the same time.
- On hot isostatic pressing was carried out at a temperature of 1155 ° C. Pressure of 105 MPa in a period of 3.85 hours, after which the compact was slowly cooled. After hot forming with 0.2 times to 8.1 times the degree of deformation was removed from the forgings of samples.
- Powders made by a method according to the invention had until to a grain diameter of 63 to account for 52% of the total and a share of approx. 72% up to a grain size of up to 100 ⁇ m. Powder according to the prior art, however, have proportions of for the same classes 21.7% and 36.2%. If one compares the determined average particle size, it is this in the case of powder production according to the invention is 61 ⁇ m, whereas in one Powder production according to the state of the art is more than twice as large average particle size of 141 ⁇ m was determined.
- Fig. 1 manufactured method according to the invention
- Fig. 2 manufactured method according to the prior art
- powders are shown in bulk.
- the comparison powder state of the Technology
- the powder produced according to the invention largely homogeneous.
- Fig. 3 pellet production according to of the invention
- Fig. 4 comparativ powder
- Tool steels of the type described can, as from the investigation Was surprisingly found, according to the invention, up to a content of 0.5 % By weight be alloyed with sulfur without the content of non-metallic Inclusions is significantly increased and a DIN K0 value of greater than 3 established.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
Description
Kohlenstoff (C) | 0,52 | bis | 3,74 |
Mangan (Mn) | bis | 2,9 | |
Chrom (Cr) | bis | 21,0 | |
Molybdän (Mo) | bis | 10,0 | |
Nickel (Ni) gegebenenfalls | bis | 1,0 | |
Kobalt (Co) | bis | 20,8 | |
Vanadin (V) | bis | 14,9 | |
Niob(Nb) Tantal (Ta) einzeln oder in Summe | bis | 2,0 | |
Wolfram (W) | bis | 20,0 | |
Schwefel (S) | bis | 0,5 |
Obige chemische Zusammensetzung des Werkzeugstahles beinhaltet besonders karbidreiche Werkzeugstähle mit hoher Abriebfestigkeit und hoher Schneidhaltigkeit der daraus gefertigten Werkzeuge. Da hohe Karbidanteile in der Regel die mechanischen Eigenschaften des Werkstoffes verschlechtern, ist deren grundsätzliche Verbesserung durch das erfindungsgemäße Verfahren von besonderer Bedeutung. Es hat sich gezeigt, daß diese hohen mechanischen Kennwerte, insbesondere die der Schlagbiegezähigkeit des Materials, synergetisch durch den kleinen mittleren Korndurchmesser des Pulvers, eine homogene dichte Schüttung desselben in der Kapsel und durch den hohen oxidischen Reinheitsgrad bei isotroper Struktur des heißisostatisch gepreßten Gegenstandes begründet sind.
Kohlenstoff (C) | 0,52 | bis | 3,74 |
Mangan (Mn) | bis | 2,9 | |
Chrom (Ce) | bis | 21,0 | |
Molybdän (Mo) | bis | 10,0 | |
Nickel (Ni) gegebenenfalls | bis | 1,0 | |
Kobalt (Co) | bis | 20,8 | |
Vanadin (V) | bis | 14,9 | |
Niob (Nb) Tantal (Ta) einzeln oder in Summe | bis | 2,0 | |
Wolfram (W) | bis | 20,0 | |
Schwefel (S) | bis | 0,5 |
Ni kann gegebenenfalls ohne nachteilige Wirkung bis zu einem Gehalt von 1,0 Gew.-% in der Legierung vorliegen
Co steigert die Warmhärte und Schneidhaltigkeit der Werkzeuge , wirkt jedoch ab einem Gehalt von 20,8 Gew.-% eigenschaftsverschlechternd.. Schwefelgehalte bis 0,5 Gew.-% verbessern die Zerspanbarkeit des Werkzeugstahles, ohne jedoch den Reinheitsgrad desselben derartig nachteilig zu beeinflussen, daß die mechanischen Materialwerte erniedrigt sind.
Kornverteilung der Metallpulver, Anteil der Partikelklassen im Metallpulver, mittlere Partikelgröße | ||
Partikelklasse Mikron | Verfahren gemäß der Erfindung Anteil in % | Vergleichsverfahren Stand der Technik Anteil in % |
0-45 | 31,5 | 12,7 |
46-63 | 20,5 | 9,0 |
64-75 | 8,7 | 5,3 |
76-100 | 11,0 | 9,2 |
101-125 | 7,6 | 9,8 |
126-180 | 9,5 | 14,0 |
181-250 | 6,0 | 13,2 |
251-355 | 3,7 | 12,8 |
355-500 | 1,5 | 14,0 |
Mittlere Partikelgröße | 61µm | 141µm |
Einschlußgehalt von PM-Werkzeugstählen K0 ( DIN 50 602) | ||||
Werkzeugstahl gem.Erfindung | Werkzeugstahl gem.Stand der Technik | |||
K0 | Anzahl der Proben | Anteil % | Anzahl der Proben | Anteil % |
0 | 28 | 56,0 | 15 | 16,3 |
1 | 18 | 36,0 | 28 | 30,4 |
2 | 3 | 6,0 | 19 | 20.7 |
3 | 1 | 2,0 | 12 | 13,0 |
4 | 7 | 7,6 | ||
5 | 2 | 2,2 | ||
6 | 3 | 3,3 | ||
7 | 1 | 1,1 | ||
8 | ||||
9 | ||||
10 | ||||
11 | ||||
12 | 1 | 1,1 | ||
13 | 1 | 1,1 | ||
14 | 1 | 1,1 | ||
15 | 1 | 1,1 | ||
16 | ||||
17 | ||||
18 | 1 | 1,1 | ||
19 | ||||
20 | ||||
Summe | 50 | 100 | 92 | 100 |
Einschlußgehalt von PM-Werkzeugstählen (ASTM E 45 /85 Meth. D) | ||||
Werkzeugstahl gem. Erfindung | Werkzeugstahl gem. Stand der Technik | |||
ASTM-Werte | Anzahl Proben | Anteil % | Anzahl Proben | Anteil % |
0,5 | 34 | 68,0 | 24 | 26,1 |
1,0 | 13 | 26,0 | 35 | 38,0 |
1,5 | 3 | 6,0 | 22 | 23,9 |
2,0 | 6 | 6,5 | ||
2,5 | 4 | 4,4 | ||
3,0 | 1 | 1,1 | ||
Summe | 50 | 100 | 92 | 100 |
Claims (15)
- Verfahren zur pulvermetallurgischen Herstellung von dichten, verformten oder unverformten Gegenständen aus Werkzeugstahl mit verbesserter Homogenität, höherer Reinheit und verbesserten Eigenschaften des Werkstoffes, wobei eine Schmelze in ein metallurgisches Gefäß eingebracht und in diesem konditioniert wird das ist ein Verbessern des oxidischen Reinheitsgrades derselben und ein Einstellen der Temperatur auf einen Wert über der Bildungstemperatur von Primärausscheidungen in der Legierung, wonach bei im wesentlichen konstant gehaltener Temperatur aus dieser Schmelze durch Verdüsung mit Stickstoff ein Pulver mit einem mittleren Korndurchmesser von 50 bis 70 µm hergestellt, im Stickstoffstrom desintegriert und unter Aufrechterhaltung der Stickstoffatmosphäre das Pulver mit einem maximalen Korndurchmesser von 500 µm klassiert, gesammelt, gemischt, in einen Behälter mit einem Durchmesser oder einer Dicke von größer als 300 mm und einer Länge von größer 1000mm eingebracht, durch mechanische Stöße in diesem verdichtet und der Behälter gasdicht verschlossen wird, worauf in einem heißisostatischen Preßzyklus für diesen die Parameter derart eingestellt werden, daß im Aufwärmvorgang die Temperatur und der Druck erhöht werden, wobei im Pulverkörper des Behältnisses bzw. der Kapsel ein allseitiger Druck von mindestens 1 bis 40 MPa wirksam ist, und danach ein isostatischer Preßvorgang bei einer Temperatur von mindestens 1100 °C, höchstens jedoch 1180°C, bei einem isostatischen Druck von mindestens 90 MPa während einer Zeitdauer von mindestens drei Stunden erfolgt und anschließend der HIP-Preßkörper gekühlt und gegebenenfalls dieser Preßkörper nachfolgend warm umgeformt und derart ein hochreiner Werkstoff mit einem gemäß DIN 50 602-K0-Wert von im wesentlichen höchstens 3 hergestellt wird.
- Verfahren nach Anspruch 1, bei welchem die Schmelze aus einer Eisenbasislegierung enthaltend in Gew.-%
Kohlenstoff (C) 0,52 bis 3,74 Mangan (Mn) bis 2,9 Chrom (Cr) bis 21,0 Molybdän (Mo) bis 10,0 Nickel (Ni) gegebenenfalls bis 1,0 Kobalt (Co) bis 20,8 Vanadin (V) bis 14,9 Niob (Nb) Tantal (Ta) einzeln oder in Summe bis 2,0 Wolfram (W) bis 20,0 Schwefel (S) bis 0,5 - Verfahren nach Anspruch 1 oder 2, bei welchem eine Konditionierung der Schmelze im metallurgischen Gefäß bei einer induzierten turbulenten Strömung derselben, vorzugsweise durch elektromagnetische Mittel, und bei einer vollständigen Abdeckung des Metallbades durch flüssige Schlacke, welche insbesondere mittels direkten Stromdurchganges beheizt wird, während eine Zeit von mindestens 15 Minuten erfolgt
- Verfahren nach Anspruch 1 bis 3, bei welchem die konditionierte Schmelze durch einen Düsenkörper im metallurgischen Gefäß mit einem Schmelzenstromdurchmesser von 4,0 bis 10,0 mm in eine Verdüsungskammer eingebracht und in dieser mit mindestens drei aufeinander folgenden aus Stickstoff, mit einem Reinheitsgrad von mind. 99.999 % Stickstoff, gebildeten Gasstrahlen mit der Maßgabe beaufschlagt wird, daß die letzte Beaufschlagung des Schmelzenstromes durch einen Gasstrahl erfolgt, der zumindest stellenweise eine Geschwindigkeit aufweist, die größer als die Schallgeschwindigkeit ist.
- Verfahren nach einem der Ansprüche 1 bis 4, bei welchem der Durchmesser der Pulverkörner verdüsungstechnisch auf einen Maximalwert von 500 µm eingestsellt oder klassiert wird.
- Verfahren nach einem der Ansprüche 1 bis 5, bei welchem das in einem Bereitstellungsraum gesammelte Pulver durch Stickstoff fluidisiert und gemischt und bei Aufrechterhaltung der Stickstoffatmosphäre in einen Behälter bzw. eine Kapsel mit einem Gesamtgewicht von größer 0,5 t eingebracht, durch mechanische Stöße verdichtet und gasdicht eingeschlossen wird.
- Verfahren nach einem der Ansprüche 1 bis 6, bei welchem das Pulver in einen Behälter bzw. eine Kapsel mit einem Durchmesser bzw. einer Dicke von gleich oder größer 400 mm und einer Länge von mindestens 1500 mm eingebracht wird.
- Verfahren nach einem der Ansprüche 1 bis 7, bei welchem die pulvergefüllte Kapsel im kalten Zustand in eine HIP-Einrichtung eingebracht wird und eine darauffolgende Erwärmung der Pulverkapsel unter allseitigem Umgebungsdruck erfolgt.
- Verfahren nach einem der Ansprüche 1 bis 8, bei welchem die Aufwärmung und/oder der Preßvorgang des Pulvers bei konstanter, gegebenenfalls sich gleichmäßig ändernder, um einem Mittelwert pendelnder Temperaturbeaufschlagung durchgeführt wird und der Preßvorgang bei einer Temperatur von mindestens 1140°C, höchstens jedoch von 1170°C, erfolgt.
- Verfahren nach einem der Ansprüche 1 bis 9, bei welchem der pulvermetallurgisch hergestellte Block im Zustand AS HIPed oder bei geringster, aus wirtschaftlichen Gründen durchzuführender Verformung als Vormaterial für Werkzeuge oder Werkzeugteile eingesetzt wird.
- Pulvermetallurgisch hergestellter Gegenstand aus Werkzeugstahl mit verbesserten Werkstoffeigenschaften, vorzugsweise hergestellt nach einem Verfahren gemäß den vorgeordneten Ansprüchen, bestehend aus einer Eisenbasislegierung enthaltend in Gew.-%
Kohlenstoff (C) 0,52 bis 3,74 Mangan (Mn) bis 2,9 Chrom (Cr) bis 21,0 Molybdän (Mo) bis 10,0 Nickel (Ni) gegebenenfalls bis 1,0 Kobalt (Co) bis 20,8 Vanadin (V) bis 14,9 Niob(Nb)/Tantal(Ta) einzeln oder in Summe bis 2,0 Wolfram (W) bis 20,0 Schwefel (S) bis 0,5 - Pulvermetallurgischer Gegenstand nach Anspruch 11, gebildet aus einem Werkstoff, welcher einen Einschlußgehalt - nach DIN 50 602 Verfahren K0- für die Summe der Kennwerte 1 und 0 einen Anteil von größer 80 % aufweist.
- Pulvermetallurgischer Gegenstand nach Anspruch 11, gebildet aus einem Werkstoff, welcher einen Einschlußgehalt - nach DIN 50 602 Verfahren K0- für den Kennwert 0 einen Anteil von größer 50 % aufweist.
- Pulvermetallurgischer Gegenstand nach Anspruch 11, gebildet aus einem Werkstoff, welcher einen Einschlußgehalt - nach ASTM E 45/85 Meth. D- für die Summe der ASTM-Werte 0,5 und 1 einen Anteil von größer 90% aufweist.
- Pulvermetallurgischer Gegenstand nach Anspruch 11, gebildet aus einem Werkstoff, welcher einen Einschlußgehalt- nach ASTM E 45/85 Meth. D- für den ASTM-Wert von 0,5 einen Anteil von größer 60 % aufweist.
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SI200130841T SI1249510T2 (sl) | 2001-04-11 | 2001-05-25 | Postopek praškasto-metalurške izdelave predmetov iz orodnega jekla |
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AT0058501A AT411580B (de) | 2001-04-11 | 2001-04-11 | Verfahren zur pulvermetallurgischen herstellung von gegenständen |
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EP1249510A2 true EP1249510A2 (de) | 2002-10-16 |
EP1249510A3 EP1249510A3 (de) | 2004-01-21 |
EP1249510B1 EP1249510B1 (de) | 2008-05-07 |
EP1249510B2 EP1249510B2 (de) | 2014-10-29 |
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EP01890158.7A Expired - Lifetime EP1249510B2 (de) | 2001-04-11 | 2001-05-25 | Verfahren zur pulvermetallurgischen Herstellung von Gegenständen aus Werkzeugstahl |
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US (1) | US6506227B1 (de) |
EP (1) | EP1249510B2 (de) |
AT (2) | AT411580B (de) |
DE (1) | DE50113936D1 (de) |
DK (1) | DK1249510T4 (de) |
ES (1) | ES2305049T5 (de) |
PT (1) | PT1249510E (de) |
SI (1) | SI1249510T2 (de) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103741042A (zh) * | 2013-12-19 | 2014-04-23 | 马鞍山市方圆材料工程有限公司 | 一种高耐磨冷轧辊用合金材料及其制备方法 |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AT409235B (de) * | 1999-01-19 | 2002-06-25 | Boehler Edelstahl | Verfahren und vorrichtung zur herstellung von metallpulver |
AT410448B (de) * | 2001-04-11 | 2003-04-25 | Boehler Edelstahl | Kaltarbeitsstahllegierung zur pulvermetallurgischen herstellung von teilen |
US20060249230A1 (en) * | 2005-05-09 | 2006-11-09 | Crucible Materials Corp. | Corrosion and wear resistant alloy |
EP3608041A1 (de) * | 2018-08-07 | 2020-02-12 | BAE SYSTEMS plc | Konsolidierung durch isostatisches heisspressen von aus pulver stammenden teilen |
WO2020030906A1 (en) * | 2018-08-07 | 2020-02-13 | Bae Systems Plc | Hot isostatic pressing consolidation of powder derived parts |
CN112279254B (zh) * | 2019-07-24 | 2022-07-15 | 比亚迪股份有限公司 | 一种碳化硅粉的制备方法及碳化硅粉 |
CN111014704B (zh) * | 2020-01-03 | 2021-01-05 | 东南大学 | 一种粉末冶金工模具钢的制备方法 |
CN116833409A (zh) * | 2021-11-29 | 2023-10-03 | 河冶科技股份有限公司 | 粉末冶金工艺制备沉淀硬化高速钢的方法 |
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EP0875588A2 (de) * | 1997-04-09 | 1998-11-04 | Crucible Materials Corporation | Kaltarbeitswerkzeugstahlteilchen mit hoher Schlagfestigkeit aus Metallpulver und Verfahren zu seiner Herstellung |
EP1022078A2 (de) * | 1999-01-19 | 2000-07-26 | BÖHLER Edelstahl GmbH | Verfahren und Vorrichtung zur Herstellung von Metallpulver durch Gasverdüsung |
EP1075886A2 (de) * | 1999-08-13 | 2001-02-14 | Crucible Materials Corporation | Heissisostatisches Pressen von hochlegiertem Stahlpulver |
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DE3338369C1 (de) * | 1983-10-21 | 1985-09-26 | Nyby Uddeholm Powder AB, Torshälla | Verfahren zur Herstellung pulvermetallurgischer Gegenstaende |
SE462837B (sv) * | 1988-07-04 | 1990-09-10 | Kloster Speedsteel Ab | Saett att pulvermetallurgiskt framstaella ett kvaevelegerat staal |
AT395230B (de) * | 1989-11-16 | 1992-10-27 | Boehler Gmbh | Verfahren zur herstellung von vormaterial fuer werkstuecke mit hohem anteil an metallverbindungen |
IT1241490B (it) * | 1990-07-17 | 1994-01-17 | Sviluppo Materiali Spa | Acciaio rapido da polveri. |
ATA240391A (de) * | 1991-12-04 | 1994-10-15 | Boehler Edelstahl | Gegenstand aus stahl für kunststofformen sowie verfahren und vorrichtung zu seiner herstellung |
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SE508872C2 (sv) * | 1997-03-11 | 1998-11-09 | Erasteel Kloster Ab | Pulvermetallurgiskt framställt stål för verktyg, verktyg framställt därav, förfarande för framställning av stål och verktyg samt användning av stålet |
US5976459A (en) * | 1998-01-06 | 1999-11-02 | Crucible Materials Corporation | Method for compacting high alloy tool steel particles |
WO1999061673A1 (en) * | 1998-05-27 | 1999-12-02 | U.S. Department Of Commerce And National Institute Of Standards And Technology | High nitrogen stainless steel |
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2001
- 2001-04-11 AT AT0058501A patent/AT411580B/de not_active IP Right Cessation
- 2001-05-25 AT AT01890158T patent/ATE394515T1/de active
- 2001-05-25 SI SI200130841T patent/SI1249510T2/sl unknown
- 2001-05-25 DK DK01890158.7T patent/DK1249510T4/en active
- 2001-05-25 DE DE50113936T patent/DE50113936D1/de not_active Expired - Lifetime
- 2001-05-25 PT PT01890158T patent/PT1249510E/pt unknown
- 2001-05-25 ES ES01890158.7T patent/ES2305049T5/es not_active Expired - Lifetime
- 2001-05-25 EP EP01890158.7A patent/EP1249510B2/de not_active Expired - Lifetime
- 2001-06-06 US US09/874,282 patent/US6506227B1/en not_active Expired - Lifetime
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EP1022078A2 (de) * | 1999-01-19 | 2000-07-26 | BÖHLER Edelstahl GmbH | Verfahren und Vorrichtung zur Herstellung von Metallpulver durch Gasverdüsung |
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103741042A (zh) * | 2013-12-19 | 2014-04-23 | 马鞍山市方圆材料工程有限公司 | 一种高耐磨冷轧辊用合金材料及其制备方法 |
CN103741042B (zh) * | 2013-12-19 | 2015-12-09 | 马鞍山市方圆材料工程有限公司 | 一种高耐磨冷轧辊用合金材料及其制备方法 |
Also Published As
Publication number | Publication date |
---|---|
AT411580B (de) | 2004-03-25 |
ES2305049T3 (es) | 2008-11-01 |
EP1249510B2 (de) | 2014-10-29 |
SI1249510T2 (sl) | 2015-02-27 |
EP1249510B1 (de) | 2008-05-07 |
DK1249510T4 (en) | 2015-02-02 |
US6506227B1 (en) | 2003-01-14 |
EP1249510A3 (de) | 2004-01-21 |
SI1249510T1 (sl) | 2008-10-31 |
DK1249510T3 (da) | 2008-09-29 |
ATE394515T1 (de) | 2008-05-15 |
PT1249510E (pt) | 2008-08-12 |
ATA5852001A (de) | 2003-08-15 |
DE50113936D1 (de) | 2008-06-19 |
ES2305049T5 (es) | 2014-12-22 |
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