EP0387237A2 - Process for making objects, tools and parts by powder metallurgy - Google Patents
Process for making objects, tools and parts by powder metallurgy Download PDFInfo
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- EP0387237A2 EP0387237A2 EP90890046A EP90890046A EP0387237A2 EP 0387237 A2 EP0387237 A2 EP 0387237A2 EP 90890046 A EP90890046 A EP 90890046A EP 90890046 A EP90890046 A EP 90890046A EP 0387237 A2 EP0387237 A2 EP 0387237A2
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/28—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases more than one element being applied in one step
- C23C8/30—Carbo-nitriding
- C23C8/32—Carbo-nitriding of ferrous surfaces
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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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
- B22F1/145—Chemical treatment, e.g. passivation or decarburisation
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12014—All metal or with adjacent metals having metal particles
- Y10T428/12028—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, etc.]
- Y10T428/12049—Nonmetal component
- Y10T428/12056—Entirely inorganic
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12535—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.] with additional, spatially distinct nonmetal component
- Y10T428/12576—Boride, carbide or nitride component
Definitions
- the invention relates to a method for the powder-metallurgical production of workpieces or tools with high-melting carbides and / or carbonitrides distributed homogeneously in the matrix and PM parts produced by this method.
- powder metallurgical processes can advantageously be used.
- a molten alloy is atomized into powder, this powder is filled into capsules and a PM part is produced by sintering, HIP-en and / or hot forming and the like.
- the invention has for its object to avoid the above disadvantages and to provide a method by which workpieces or tools with high-melting carbides, nitrides and / or carbonitrides of the elements of the IV and V group or sub-group of the periodic system with a small grain size, which are distributed homogeneously in the matrix.
- the carbon and nitrogen content of the molten alloy, which is atomized into powder be set below a limit which is dependent on the total concentration of the elements of the IVth and Vth group of the periodic system and to set a desired carbon and / or nitrogen content
- the atomization medium contains carbon compounds and / or nitrogen and / or a diffusion annealing of the powder at a temperature of at least the austenitizing temperature, but at most 50 ° C below the softening temperature of the alloy, and this annealing is carried out, if necessary, at certain contents or partial pressures of gaseous carbon compounds and / or nitrogen, in particular when the powder flows through it.
- a particular advantage is given when two or more powders with different compositions and / or different carbon and nitrogen contents produced by the process according to the invention are mixed homogeneously and a PM part is produced from this mixed powder, because this results in an optimal setting of the composition or the usage properties of the part is achieved with low storage or at low costs.
- the zone near the surface of the powder grains can absorb carbon and nitrogen to a corresponding extent and that this effect with a grain surface area of less than 0 , 9 mm2 is particularly effective. It was surprising for the person skilled in the art that a powder, also by annealing the powder in a z. enrichment of carbon and / or nitrogen in the hydrocarbon and / or nitrogen-containing atmosphere in the zone near the grain surface can be compensated for by diffusion annealing or by sintering, HIP-en and hot rolling, the carbides migrating into the grain interior melting carbides and / or form carbonitrides. The carbides and / or carbonitrides formed are homogeneously distributed and have a very small grain size. There is currently no scientific justification for this effect, but it is conceivable that one of the causes is different diffusion rates of different atoms.
- the part formed into a tool had a carbon content of 1.32% by weight and a nitrogen concentration of 26o ppm, the grain size of the carbides and carbonitrides mainly containing vanadium and niobium at a maximum of 5 ⁇ m Was 11 vol .-%.
- the tool had significantly improved properties compared to conventionally manufactured high-speed steel S 6-5-1-3 Nb with toughness values improved by approx. 28%.
- the PM part with a C content of 1.70% was processed into a milling tool, heat-treated and with a hard material layer made of TiN with a thickness of 3 ⁇ m according to the PVD process Mistake.
- a forming tool which is particularly subject to abrasion, was produced from the 2.64% by weight carbon-containing PM part and coated in multiple layers with Ti (CN) hard material.
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- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General 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
Die Erfindung betrifft ein Verfahren zur pulvermetallurgischen Herstellung von Werkstücken oder Werkzeugen mit in der Matrix homogen verteilten, hochschmelzenden Karbiden und/oder Karbonitriden und nach diesem Verfahren hergestellte PM-Teile.The invention relates to a method for the powder-metallurgical production of workpieces or tools with high-melting carbides and / or carbonitrides distributed homogeneously in the matrix and PM parts produced by this method.
Bei der Herstellung von Werkstücken oder Werkzeugen, insbesondere aus Legierungen mit hohem Kohlenstoffgehalt wie beispielsweise Kaltarbeitsstähle, Schnellstähle und dgl. und/oder hoher Stickstoffkonzentration können vorteilhaft pulvermetallurgische Verfahren angewendet werden. Dabei wird eine geschmolzene Legierung zu Pulver verdüst, dieses Pulver in Kapseln gefüllt und durch Sintern, HIP-en und/oder Warmumformen und dgl. ein PM- Teil hergestellt. Bei einer raschen Abkühlung der beim Verdüsen einer homogenen Schmelze entstehenden Teilchen steht für eine Reaktion des Kohlenstoffes und/oder Stickstoffes mit karbidbildenden und/oder nitridbildenden Elementen der Legierung nur eine kurze Zeitspanne zur Verfügung, sodaß ein Wachsen von groben Karbiden und/oder Karbonitriden während der Erstarrung verhindert und eine gleichmäßige Verteilung von feinen Partikeln dieser Verbindungen in den Pulverkörnern erzielt wird. Die gefertigten PM-Teile weisen dadurch eine homogene Verteilung von Karbiden und /oder Karbonitriden mit geringer Korngröße in einer Matrix auf, wodurch insbesondere die Zähigkeit und die Gebrauchseigenschaften verbessert sind.In the production of workpieces or tools, in particular from alloys with a high carbon content such as cold work steels, high-speed steels and the like and / or high nitrogen concentration, powder metallurgical processes can advantageously be used. A molten alloy is atomized into powder, this powder is filled into capsules and a PM part is produced by sintering, HIP-en and / or hot forming and the like. In the case of rapid cooling of the particles formed when atomizing a homogeneous melt, there is only a short period of time available for a reaction of the carbon and / or nitrogen with carbide-forming and / or nitride-forming elements of the alloy, so that coarse carbides and / or carbonitrides grow during the Solidification is prevented and an even distribution of fine particles of these compounds in the powder grains is achieved. The PM parts produced thereby have a homogeneous distribution of carbides and / or carbonitrides with a small grain size in a matrix, which in particular improves the toughness and the properties of use.
Die anwendbaren Gehalte an Kohlenstoff und/oder Stickstoff in Verbindung mit den Gehalten an karbid- und/oder nitridbildenden Elementen der IV. und V. Gruppe bzw. Nebengruppe des periodischen Systems der Legierung sind jedoch begrenzt, weil bei höheren Konzentrationen auf Grund einer hohen Affinität dieser Elemente zu Kohlenstoff und/oder Stickstoff schon in der flüssigen Schmelze Karbide und/oder Karbonitride gebildet werden. Diese primär ausgeschiedenen Verbindungen weisen einen hohen Schmelzpunkt auf und wachsen in der Schmelze zu großen, meist blockigen und/oder dendritischen Körnern, welche auch durch einen Verdüsungsvorgang nicht zerkleinert werden können. Dadurch können Inhomogenitäten mit Kerbstellen von groben Karbiden im nachfolgend gefertigten PM-Teil entstehen, die dessen Gebrauchseigenschaften, insbesondere dessen Zähigkeit, negativ beeinflussen.The applicable levels of carbon and / or nitrogen in conjunction with the levels of carbide- and / or nitride-forming elements of the IV and V group or sub-group of the periodic Systems of the alloy are limited, however, because at higher concentrations, due to the high affinity of these elements for carbon and / or nitrogen, carbides and / or carbonitrides are formed in the liquid melt. These primarily excreted compounds have a high melting point and grow in the melt to form large, usually blocky and / or dendritic grains, which cannot be comminuted by a spraying process. This can result in inhomogeneities with notches of coarse carbides in the subsequently manufactured PM part, which negatively influence its performance properties, in particular its toughness.
Es wurde versucht, bei höheren Konzentrationen, insbesondere der Elemente C und Nb, durch legierungstechnische Maßnahmen bzw. durch Beeinflussung des Keimzustandes der Schmelze die Bildung von groben primären Karbidausscheidungen zu vermeiden, jedoch konnten dadurch keine wesentlichen Verbesserungen erreicht werden.Attempts were made to avoid the formation of coarse primary carbide precipitates at higher concentrations, in particular of the elements C and Nb, by alloying measures or by influencing the germ state of the melt, but no significant improvements could be achieved thereby.
Auch wurde vorgeschlagen, Legierungen mit Konzentrationen an Elementen, die Karbide vom Typ MeC und Me₄C₃ bilden, von über 3,0 Gew.-% weit über die üblichen Schmelzentemperaturen, beispielsweise auf 1750°bis 1800°C, zu überhitzen, dadurch primäre Ausscheidungen von Karbiden aufzulösen bzw. zu vermeiden und von dieser Temperatur die Legierung rasch abzukühlen. Dies hat den Nachteil, daß es zu einem raschen Verschleiß der feuerfesten Auskleidungen der Schmelz- und Verdüsungsaggregate kommt. Weiters wird bei hohen Temperaturen die Affinität der Elemente, beispielsweise des Niobs und des Titans zu Sauerstoff wesentlich erhöht, sodaß es zu vermehrten Oxidbildungen, zu Verunreinigungen der Schmelze und zu einem unkontrollierbaren Abbrand der Elemente kommt.It has also been proposed to overheat alloys with concentrations of elements which form carbides of the MeC and Me₄C₃ type, from over 3.0% by weight well above the usual melt temperatures, for example to 1750 ° to 1800 ° C, thereby causing primary precipitates Dissolve or avoid carbides and quickly cool the alloy from this temperature. This has the disadvantage that the refractory linings of the melting and atomizing units wear out rapidly. Furthermore, the affinity of the elements, for example niobium and titanium, to oxygen is increased significantly at high temperatures, so that there is increased oxide formation, contamination of the melt and uncontrollable erosion of the elements.
Der Erfindung liegt die Aufgabe zugrunde, obige Nachteile zu vermeiden und ein Verfahren zu schaffen, nach welchem Werkstücke oder Werkzeuge mit in der Matrix homogen verteilten hochschmelzenden Karbiden, Nitriden und/oder Karbonitriden der Elemente der IV. und V. Gruppe bzw. Nebengruppe des periodischen Systems mit geringer Korngröße hergestellt werden können.The invention has for its object to avoid the above disadvantages and to provide a method by which workpieces or tools with high-melting carbides, nitrides and / or carbonitrides of the elements of the IV and V group or sub-group of the periodic system with a small grain size, which are distributed homogeneously in the matrix.
Diese Aufgabe wird erfindungsgemäß durch das in Anspruch 1 gekennzeichnete Verfahren gelöst. Dabei ist wichtig, daß der Kohlenstoff-und Stickstoffgehalt der geschmolzenen Legierung, welche zu Pulver verdüst wird, unter einer von der Gesamtkonzentration der Elemente der IV. und V. Gruppe des periodischen Systems abhängigen Grenze eingestellt werden und zur Einstellung eines gewünschten Kohlenstoff-und/oder Stickstoffgehaltes das Verdüsungsmedium Kohlenstoffverbindungen und/oder Stickstoff enthält und/oder eine Diffusionsglühung des Pulvers bei einer Temperatur von mindestens der Austenitisierungstemperatur, höchstens jedoch 50°C unterhalb der Erweichungstemperatur der Legierung erfolgt und diese Glühung gegebenenfalls bei bestimmten Gehalten bzw. Partialdrücken von gasförmigen Kohlenstoffverbindungen und/oder Stickstoff, insbesondere bei Durchströmung des Pulvers, durchgeführt wird. Ein besonderer Vorteil ist gegeben, wenn zwei oder mehrere nach dem erfindungsgemäßen Verfahren herstellte Pulver mit unterschiedlichen Zusammensetzungen und/oder verschiedenen Kohlenstoff-und Stickstoffgehalten homogen vermischt werden und eine Herstellung eines PM-Teiles aus diesem gemischten Pulver erfolgt, weil dadurch eine optimale Einstellung der Zusammensetzung bzw. der Gebrauchseigenschaften des Teiles bei geringer Lagerhaltung bzw. bei geringen Kosten erreicht wird.This object is achieved according to the invention by the method characterized in claim 1. It is important that the carbon and nitrogen content of the molten alloy, which is atomized into powder, be set below a limit which is dependent on the total concentration of the elements of the IVth and Vth group of the periodic system and to set a desired carbon and / or nitrogen content, the atomization medium contains carbon compounds and / or nitrogen and / or a diffusion annealing of the powder at a temperature of at least the austenitizing temperature, but at most 50 ° C below the softening temperature of the alloy, and this annealing is carried out, if necessary, at certain contents or partial pressures of gaseous carbon compounds and / or nitrogen, in particular when the powder flows through it. A particular advantage is given when two or more powders with different compositions and / or different carbon and nitrogen contents produced by the process according to the invention are mixed homogeneously and a PM part is produced from this mixed powder, because this results in an optimal setting of the composition or the usage properties of the part is achieved with low storage or at low costs.
Es hat sich gezeigt, daß auch bei Konzentrationen an, insbesondere mehreren Elementen der IV. und V. Gruppe bzw. Nebengruppe des periodischen Systems, von größer als 3 Gew.-% durch eine Erniedrigung des Kohlenstoffgehaltes der Legierung eine Ausscheidung von Karbiden und Karbonitriden aus einer Schmelze verhindert wird. Ab einem Mindestgehalt dieser Elemente ist eine gegenseitige Beeinflussung gegeben, wodurch die oberen Grenzwerte für Kohlenstoff und Stickstoff , ab welchen eine Karbid- und/oder Karbonitridausscheidung erfolgen kann , bestimmt und errechenbar sind. Unerwarteterweise wurde gefunden, daß bei einer Verdüsung der flüssigen Legierung unter Verwendung von flüssigen und/oder gasförmigen kohenwasserstoff-und/oder stickstoffhältigen Verdüsungsmedien die oberflächennahe Zone der Pulverkörner in entsprechendem Maße Kohlenstoff und Stickstoff aufnehmen kann und daß dieser Effekt bei einer Kornoberfläche von kleiner als 0,9 mm² besonders wirkungsvoll ist. Für den Fachmann war überraschend, daß eine auch durch Glühung des Pulvers in einer z,B. kohlenwasserstoff-und/oder stickstoffhältigen Atmosphäre herstellbare Anreicherung von Kohlenstoff und/oder Stickstoff in der kornoberflächennahen Zone durch eine Diffusionsglühung oder bei einem Sintern, HIP-en und Warmwalzen ausgeglichen werden kann,wobei die in das Korninnere wandernden Kohlenstoff-und/oder Stickstoffatome hochschmelzende Karbide und/oder Karbonitride bilden. Diese gebildeten Karbide und/oder Karbonitride sind homogen verteilt und weisen eine sehr geringe Korngröße auf. Für diesen Effekt fehlt derzeit noch eine wissenschaftliche Begründung, es ist jedoch vorstellbar, daß eine der Ursachen unterschiedliche Diffusionsgeschwindigkeiten verschiedener Atome ist.It has been shown that even at concentrations of, in particular, several elements of the IV and V groups or subgroups of the periodic system of greater than 3% by weight, a decrease in the carbon content of the alloy causes carbides and carbonitrides to be precipitated a melt is prevented. From a minimum content of these elements, there is a mutual influence, as a result of which the upper limit values for carbon and nitrogen, from which carbide and / or carbonitride precipitation can take place, are determined and calculable. It was unexpectedly found that when atomizing the liquid alloy using liquid and / or gaseous hydrocarbon and / or nitrogen-containing atomizing media, the zone near the surface of the powder grains can absorb carbon and nitrogen to a corresponding extent and that this effect with a grain surface area of less than 0 , 9 mm² is particularly effective. It was surprising for the person skilled in the art that a powder, also by annealing the powder in a z. enrichment of carbon and / or nitrogen in the hydrocarbon and / or nitrogen-containing atmosphere in the zone near the grain surface can be compensated for by diffusion annealing or by sintering, HIP-en and hot rolling, the carbides migrating into the grain interior melting carbides and / or form carbonitrides. The carbides and / or carbonitrides formed are homogeneously distributed and have a very small grain size. There is currently no scientific justification for this effect, but it is conceivable that one of the causes is different diffusion rates of different atoms.
Bei Überwindung von Vorurteilen der Fachwelt wurde auch gefunden, daß ein homogener PM-Teil oder ein Werkzeug mit gleichmäßiger Verteilung von Karbiden und/oder Nitriden mit einer Korngröße von kleiner 5µm aus Mischungen von unterschiedlich zusammengesetzten oder verschiedene Kohlenstoffgehalte und/oder Stickstoffgehalte aufweisenden Pulvern erzeugt werden kann, wenn die Oberfläche der Pulverkörner kleiner als 0,9 mm² ist. Bei der Erprobung derartiger PM-Teile wurde weiters gefunden, daß besonders gute mechanische Eigenschaften des Werkstoffes bzw. Werkzeuges bei hohen Karbid und/oder Karbonitridanteilen vorlagen.While overcoming prejudices among experts, it was also found that a homogeneous PM part or a tool with a uniform distribution of carbides and / or nitrides with a grain size of less than 5 μm is produced from mixtures of powders with different compositions or with different carbon contents and / or nitrogen contents can if the surface of the powder grains is smaller than 0.9 mm². When testing such PM parts, it was also found that there were particularly good mechanical properties of the material or tool with high carbide and / or carbonitride contents.
Die Erfindung wird nachfolgend anhand von Ausführungsbeispielen weiter erläutert:The invention is further explained below using exemplary embodiments:
Eine Legierung mit nachfolgend angegebener Zusammensetzung in Gew.-%
C = 0,75
W = 6,64
Mo = 4,80
Cr = 4,76
V = 1,16,
Nb = 3,14
und einer N- Konzentration von 30 ppm, Rest im wesentlichen Fe, wurde erschmolzen.
Eine Untersuchung von Saugproben, die bei einer Temperatur von 1450 C der Schmelze entnommen wurden, zeigte keine primären Karbid-oder Karbonitridausscheidungen.
Die Schmelze wurde mittels eines Mediums aus Helium, Stickstoff und Härteöl zu Pulver verdüst, wobei die Oberfläche der größeren Pulverkörner 0,6 mm² betrug. Nach dem Kompaktieren, Heißisostatikpressen und Verformen des Pulvers wies der zu einem Werkzeug geformte Teil einen Kohlenstoffgehalt von 1,32 Gew.-% und eine Stickstoffkonzentration von 26o ppm auf, wobei die Korngröße der hauptsächlich Vanadin und Niob enthaltenden Karbide und Karbonitride maximal 5µm bei einem Anteil von 11 Vol.-% betrug. Das Werkzeug wies im wärmebehandelten Zustand im Vergleich mit konventionell hergestelltem Schnellstahl S 6-5-1-3 Nb wesentlich verbesserte Gebrauchseigenschaften bei um ca. 28 % verbesserten Zähigkeitwerten auf.An alloy with the following composition in% by weight
C = 0.75
W = 6.64
Mo = 4.80
Cr = 4.76
V = 1.16,
Nb = 3.14
and an N concentration of 30 ppm, balance essentially Fe, was melted.
An examination of suction samples, which were taken from the melt at a temperature of 1450 C, showed no primary carbide or carbonitride precipitations.
The melt was atomized to powder using a medium of helium, nitrogen and hardening oil, the surface of the larger powder grains being 0.6 mm 2. After compacting, hot isostatic pressing and shaping of the powder, the part formed into a tool had a carbon content of 1.32% by weight and a nitrogen concentration of 26o ppm, the grain size of the carbides and carbonitrides mainly containing vanadium and niobium at a maximum of 5 µm Was 11 vol .-%. In the heat-treated state, the tool had significantly improved properties compared to conventionally manufactured high-speed steel S 6-5-1-3 Nb with toughness values improved by approx. 28%.
In einem Induktionsofen wurde eine Legierung mit folgender Zusammensetzung in Gew.-% geschmolzen:
C = 0,56
Si = 0,44
Mn = 0,52
P = 0,003
S = 0,0029
Cr = 4,50
Mo = 3,70
W = 2,40
V = 1,76
Nb = 3,22
Ti = 1,74
Rest Eisen
Der Stickstoffgehalt betrug 50 ppm; bei 1440°C konnten keine primären Karbid,- Karbonitrid -oder Nitridausscheidungen festgestellt werden. Das Verdüsen der Schmelze zu Pulver mit einer maximalen Kornoberfläche von 0,65 mm² erfolgte mit Methan, worauf das Pulver bei einer Temperatur von 910°C bei Durchströmung eines aus Endogas bestehenden Gasgemisches diffusionsgeglüht wurde. Nach der Weiterverarbeitung dieses in einer evakuierten Kapsel befindlichen Pulvers durch Warmverformung bei einer Temperatur von 1185°C zu einem PM-Teil wurde dieser nach einer entsprechenden Wärmebehandlung untersucht. Die Materialerprobungen ergaben folgende Werte: Kohlenstoffgehalt 1,48 Gew.-%, Stickstoffgehalt 250 ppm, maximale Korngröße der hauptsächlich Vanadin, Niob und Titan enthaltenden ( mit Röntgenspektralanalyse festgestellt) Karbide, Karbonitride und Nitride 4,5µm, Karbid,-Karbonitrid-und Nitridanteil 13 Vol.-%.In an induction furnace, an alloy with the following composition was melted in% by weight:
C = 0.56
Si = 0.44
Mn = 0.52
P = 0.003
S = 0.0029
Cr = 4.50
Mo = 3.70
W = 2.40
V = 1.76
Nb = 3.22
Ti = 1.74
Rest of iron
The nitrogen content was 50 ppm; At 1440 ° C no primary carbide, carbonitride or nitride deposits were found. The melt was atomized into powder with a maximum grain surface area of 0.65 mm 2 using methane, whereupon the powder was diffusion-annealed at a temperature of 910 ° C. while flowing through a gas mixture consisting of endogas. After further processing of this powder, which was in an evacuated capsule, by thermoforming at a temperature of 1185 ° C. to form a PM part, it was examined after a corresponding heat treatment. The material tests yielded the following values: carbon content 1.48% by weight, nitrogen content 250 ppm, maximum grain size of the carbides, carbonitrides and nitrides 4.5 μm, which mainly contain vanadium, niobium and titanium (determined by X-ray spectral analysis), carbide, carbonitride and nitride content 13 vol%.
In einem Ofen wurde eine Legierung vorerst unter Vakuum und in der Folge unter Schutzgas mit einer Zusammensetzung in Gew.-% von C = 0,78
Si = 0,52
Mn = 0,34
P = 0,003
S = 0,0025
Cr = 4,6
Mo = 3,74
W = 2,86
V = 2,14
Nb = 6,9
Ti = 0,86
Rest Eisen
erschmolzen und anschließend mit Stickstoff zu Pulver mit einer Teilchenoberfläche von durchschnittlich 0,18 mm² verdüst.In einer Glüheinrichtung erfolgte an einem Teil des Pulvers eine Glühung bei 1210°C mit durchströmendem Methan- Stickstoff-Gasgemisch, wonach dessen Kohlenstoffgehalt 2,64 Gew.-% betrugAn alloy was initially in a furnace under vacuum and then under protective gas with a composition in% by weight of C = 0.78
Si = 0.52
Mn = 0.34
P = 0.003
S = 0.0025
Cr = 4.6
Mo = 3.74
W = 2.86
V = 2.14
Nb = 6.9
Ti = 0.86
Rest of iron
melted and then atomized with nitrogen to form a powder with a particle surface area of 0.18 mm². In an annealing device, part of the powder was annealed at 1210 ° C with a flowing methane-nitrogen gas mixture, after which its carbon content was 2.64% by weight. % amounted to
Aus dem verdüsten Pulver ( 0,78 % C), aus dem verdüsten und geglühten Pulver ( 2,64%C) und aus einem im Verhältnis von ca. 50 : 50 gemischten Pulver ( 1,70% C) wurden durch HIP-en und anschließendes Verformen PM-Teile und Werkzeuge gefertigt. Gefügeuntersuchungen erbrachten, daß in allen Teilen eine gleichmäßige Verteilung von Karbiden und Karbonitriden mit einer maximalen Korngröße von 3,5µm vorlag. Der Karbid-und Karbonitridanteil des Werkstoffes mit einem Gehalt von 0,78 % C war 6 Vol.-%, jener des Werkstoffes mit 1,70 % C war 14 Vol.-% , wobei der PM-Teil mit 2,64 % C einen Karbid-und Karbonitridanteil von ca. 21 % aufwies. Aus dem Werkstoff mit der Kohlenstoffkonzentration von 0,78 Gew.-% wurde eine eine besonders hohe Materialzähigkeit aufweisender Fließpreßstempel gefertigt. welcher im praktischen Einsatz eine Leistungssteigerung im Vergleich mit Kaltarbeitsstahl von 285 % erbrachte.From the atomized powder (0.78% C), from the atomized and annealed powder (2.64% C) and from a powder mixed in a ratio of approx. 50:50 (1.70% C) were by HIP-en and then deforming PM parts and tools. Structural studies showed that there was an even distribution of carbides and carbonitrides with a maximum grain size of 3.5 µm in all parts. The carbide and carbonitride content of the material with a content of 0.78% C was 6 vol.%, That of the material with 1.70% C was 14 vol.%, The PM part with 2.64% C. had a carbide and carbonitride content of approximately 21%. An extrusion die with a particularly high material toughness was produced from the material with the carbon concentration of 0.78% by weight. which resulted in a performance increase of 285% in comparison to cold work steel.
Der PM-Teil mit einem C-Gehalt von 1,70 % wurde zu einem Fräswerkzeug weiterverarbeitet, wärmebehandelt und mit einer Hartstoffschicht aus TiN mit einer Stärke von 3µm nach dem PVD-Verfahren versehen. Die Standzeit des Fräsers, auch bei unterbrochenem Schnitt, war wesentlich erhöht, wobei eine besonders gute Haftung der TiN-Beschichtung vorlag.The PM part with a C content of 1.70% was processed into a milling tool, heat-treated and with a hard material layer made of TiN with a thickness of 3 µm according to the PVD process Mistake. The service life of the milling cutter, even when the cut was interrupted, was significantly increased, and the TiN coating had particularly good adhesion.
Ein, insbesondere auf Abrieb beanspruchtes, Umformwerkzeug wurde aus dem 2,64 Gew.-% Kohlenstoff aufweisenden PM-Teil gefertigt und mehrlagig mit Ti(CN)-Hartstoff beschichtet. Die gute Haftung der Hartstoffschicht sowie die ausgezeichneten mechanischen Eigenschaften in der Kombination von hoher Härte und hoher Abriebfestigkeit durch den hohen Karbidanteil bei guter Materialzähigkeit führte im praktischen Gebrauch des Umformwerkzeuges zu überlegenen Standzeiten.A forming tool, which is particularly subject to abrasion, was produced from the 2.64% by weight carbon-containing PM part and coated in multiple layers with Ti (CN) hard material. The good adhesion of the hard material layer as well as the excellent mechanical properties in the combination of high hardness and high abrasion resistance due to the high carbide content with good material toughness led to superior tool life in practical use of the forming tool.
Claims (9)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT491/89 | 1989-03-06 | ||
AT491/89A AT392929B (en) | 1989-03-06 | 1989-03-06 | METHOD FOR THE POWDER METALLURGICAL PRODUCTION OF WORKPIECES OR TOOLS |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0387237A2 true EP0387237A2 (en) | 1990-09-12 |
EP0387237A3 EP0387237A3 (en) | 1991-01-23 |
Family
ID=3492022
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP19900890046 Withdrawn EP0387237A3 (en) | 1989-03-06 | 1990-02-22 | Process for making objects, tools and parts by powder metallurgy |
Country Status (5)
Country | Link |
---|---|
US (1) | US5034282A (en) |
EP (1) | EP0387237A3 (en) |
JP (1) | JPH02282436A (en) |
KR (1) | KR900014613A (en) |
AT (1) | AT392929B (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5238482A (en) * | 1991-05-22 | 1993-08-24 | Crucible Materials Corporation | Prealloyed high-vanadium, cold work tool steel particles and methods for producing the same |
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US5256368A (en) * | 1992-07-31 | 1993-10-26 | The United States Of America As Represented By The Secretary Of The Interior | Pressure-reaction synthesis of titanium composite materials |
US5669059A (en) * | 1994-01-19 | 1997-09-16 | Alyn Corporation | Metal matrix compositions and method of manufacturing thereof |
US5980602A (en) * | 1994-01-19 | 1999-11-09 | Alyn Corporation | Metal matrix composite |
US5722033A (en) * | 1994-01-19 | 1998-02-24 | Alyn Corporation | Fabrication methods for metal matrix composites |
CN1123192A (en) * | 1994-11-15 | 1996-05-29 | 郝相臣 | Method for making filtering component and product thereof |
GB2315441B (en) * | 1996-07-20 | 2000-07-12 | Special Melted Products Limite | Production of metal billets |
CN103551573B (en) * | 2013-10-22 | 2015-06-17 | 中国科学院金属研究所 | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process |
US10794210B2 (en) | 2014-06-09 | 2020-10-06 | Raytheon Technologies Corporation | Stiffness controlled abradeable seal system and methods of making same |
WO2023144592A1 (en) * | 2022-01-31 | 2023-08-03 | Arcelormittal | Ferrous alloy powder for additive manufacturing |
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GB2048955A (en) * | 1979-04-05 | 1980-12-17 | Atomic Energy Authority Uk | Titanium Nitride Strengthened Alloys |
EP0156760A2 (en) * | 1984-03-12 | 1985-10-02 | MANNESMANN Aktiengesellschaft | Process and apparatus for the manufacturing of hot-working tools |
JPS6415344A (en) * | 1987-07-07 | 1989-01-19 | Mitsubishi Metal Corp | Manufacture of sintered high-speed steel member |
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DE2732966A1 (en) * | 1977-07-21 | 1979-02-01 | Rutger Larson Konsult Ab | Metal powder prodn. - by atomising molten metal stream through pressurised agent jets and collecting droplets in reducing fluid |
US4609526A (en) * | 1984-05-14 | 1986-09-02 | Crucible Materials Corporation | Method for compacting alloy powder |
US4639352A (en) * | 1985-05-29 | 1987-01-27 | Sumitomo Electric Industries, Ltd. | Hard alloy containing molybdenum |
US4857108A (en) * | 1986-11-20 | 1989-08-15 | Sandvik Ab | Cemented carbonitride alloy with improved plastic deformation resistance |
US4891338A (en) * | 1987-01-13 | 1990-01-02 | Lanxide Technology Company, Lp | Production of metal carbide articles |
US4942097A (en) * | 1987-10-14 | 1990-07-17 | Kennametal Inc. | Cermet cutting tool |
DE3806602A1 (en) * | 1988-03-02 | 1988-07-07 | Krupp Gmbh | CARBIDE BODY |
CA1319497C (en) * | 1988-04-12 | 1993-06-29 | Minoru Nakano | Surface-coated cemented carbide and a process for the production of the same |
EP0417333B1 (en) * | 1989-09-11 | 1996-12-27 | Mitsubishi Materials Corporation | Cermet and process of producing the same |
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1989
- 1989-03-06 AT AT491/89A patent/AT392929B/en not_active IP Right Cessation
-
1990
- 1990-02-22 EP EP19900890046 patent/EP0387237A3/en not_active Withdrawn
- 1990-03-01 JP JP2047400A patent/JPH02282436A/en active Pending
- 1990-03-03 KR KR1019900002885A patent/KR900014613A/en not_active Application Discontinuation
- 1990-03-05 US US07/487,048 patent/US5034282A/en not_active Expired - Fee Related
Patent Citations (3)
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GB2048955A (en) * | 1979-04-05 | 1980-12-17 | Atomic Energy Authority Uk | Titanium Nitride Strengthened Alloys |
EP0156760A2 (en) * | 1984-03-12 | 1985-10-02 | MANNESMANN Aktiengesellschaft | Process and apparatus for the manufacturing of hot-working tools |
JPS6415344A (en) * | 1987-07-07 | 1989-01-19 | Mitsubishi Metal Corp | Manufacture of sintered high-speed steel member |
Non-Patent Citations (1)
Title |
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PATENT ABSTRACTS OF JAPAN, Band 13, Nr. 190 (C-593)[3538], 8. Mai 1989; & JP-A-01 015 344 (MITSUBISHI METAL CORP.) (19-01-1989) * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
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US5238482A (en) * | 1991-05-22 | 1993-08-24 | Crucible Materials Corporation | Prealloyed high-vanadium, cold work tool steel particles and methods for producing the same |
US5344477A (en) * | 1991-05-22 | 1994-09-06 | Crucible Materials Corporation | Prealloyed high-vanadium, cold work tool steel particles |
Also Published As
Publication number | Publication date |
---|---|
US5034282A (en) | 1991-07-23 |
JPH02282436A (en) | 1990-11-20 |
KR900014613A (en) | 1990-10-24 |
ATA49189A (en) | 1990-12-15 |
AT392929B (en) | 1991-07-10 |
EP0387237A3 (en) | 1991-01-23 |
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