EP0779937B1 - Process for case hardening higher molybdenum-alloyed sintered steels - Google Patents
Process for case hardening higher molybdenum-alloyed sintered steels Download PDFInfo
- Publication number
- EP0779937B1 EP0779937B1 EP96919584A EP96919584A EP0779937B1 EP 0779937 B1 EP0779937 B1 EP 0779937B1 EP 96919584 A EP96919584 A EP 96919584A EP 96919584 A EP96919584 A EP 96919584A EP 0779937 B1 EP0779937 B1 EP 0779937B1
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- EP
- European Patent Office
- Prior art keywords
- sintered
- molybdenum
- heat treatment
- iron
- sintering
- 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
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Classifications
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1003—Use of special medium during sintering, e.g. sintering aid
- B22F3/1007—Atmosphere
- B22F3/101—Changing atmosphere
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/78—Combined heat-treatments not provided for above
-
- 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
- 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
- C23C8/08—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 only one element being applied
- C23C8/20—Carburising
-
- 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
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/01—Reducing atmosphere
- B22F2201/013—Hydrogen
-
- 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
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/20—Use of vacuum
-
- 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
- B22F2201/00—Treatment under specific atmosphere
- B22F2201/30—Carburising atmosphere
Definitions
- the invention relates to a method for case hardening higher molybdenum alloyed sintered steels.
- the inventive method with the in claim 1 offers the advantage that higher molybdenum alloyed sintered steels are case hardened can without the formation of a brittle Carbide net is coming.
- the additional heat treatment is applied immediately after the sintering is carried out in one step, the Protective gas atmosphere present during sintering or the vacuum through a carbon donor Means, that is, carbon-containing atmosphere, is replaced.
- the presence of one Minimum proportion of ⁇ iron of 40% for case hardening Sintered steels necessary. would be from room temperature hoisted, the supply of carbon during the High heating can be blocked because it is also below the two-phase area only ⁇ -iron is present (see Figure 2) and the harmful iron carbide is created in this area would.
- a long heating-up phase would be necessary ultimately represents a dead process time.
- To avoid this dead time is from the sintering temperature to the Temperature of the two-phase area ( ⁇ and ⁇ iron) cooled down. This also makes the sintering process supplied thermal energy is used.
- the heat treatment is preferably at a temperature of 1120 ° C, 40% of the Material volume of the higher molybdenum alloyed sintered steel in the necessary lattice structure area of the ⁇ -iron, if the Molybdenum content is 3.5% by weight. This will make the initial intake of carbon favors.
- case hardening in addition to the additional heat treatment after sintering then the case hardening in the usual Carry out case hardening temperatures of 840 to 950 ° C. This ensures that by means of between the Sintering and case hardening performed additional Heat treatment activates the higher molybdenum alloy Sintered steel takes place so that the installation of carbon becomes possible without it forming a brittle Carbide network is coming.
- FIG. 1 shows a block diagram of the method for Case hardening of higher molybdenum alloyed sintered steels
- Figure 2 is a state diagram of molybdenum alloys Sintered steels.
- a first method step 10 the in Molybdenum-containing steel in powder form Molded body of any geometric shape pressed.
- the molybdenum content of the steel is, for example, 3.5%.
- a second method step 12 then takes place Sintering of the previously pressed molded body at a Sintering temperature of 1250 ° C.
- Sintered material such as that shown in Figure 2
- State diagram of sintered steels containing molybdenum Höganäs is illustrated exclusively in Lattice structure area of the ⁇ -iron.
- the sintering takes place under a protective gas atmosphere, for example under Hydrogen or in a vacuum.
- a next method step 14 the previous one sintered higher molybdenum alloy sintered steel of another Heat treatment at a temperature of, for example Subjected to 1120 ° C.
- This heat treatment takes place under supply of carbon-containing atmosphere instead.
- the Sintered steel expediently from the sintering temperature cooled down.
- the heat treatment takes place immediately after sintering.
- Case hardening of the previously sintered and according Process step 14 heat treated higher molybdenum alloys Sintered steel.
- This case hardening takes place at temperatures from 840 ° C to 950 ° C while supplying the carbonaceous Atmosphere or other - not to be considered here - carbon donor.
- the molybdenum alloy was thus activated Sintered steel, so that by case hardening in the Method step 18 also among those given here lower temperatures the installation of carbon in the Edge zones of the molded body is possible without it Formation comes from a brittle carbide network.
- a special one designated 16 here Use can be supplied.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
Description
Die Erfindung betrifft ein Verfahren zum Einsatzhärten von höhermolybdänlegierten Sinterstählen.The invention relates to a method for case hardening higher molybdenum alloyed sintered steels.
Es ist bekannt, aus metallischen Pulvern, beispielsweise aus Stahlpulvern, durch Sintern Formkörper beliebiger Geometrie herzustellen. Die metallischen Pulver werden hierbei unter einer bestimmten Temperatur, die wenig unter dem Schmelzpunkt der Sintermaterialien liegt, wärmebehandelt. Bei der Wärmebehandlung von Sinterstählen stellen sich bekannterweise Bereiche mit unterschiedlichen Gitterstrukturen ein, in denen sich sogenanntes α-Eisen, γ-Eisen oder eine Mischstruktur aus α- und γ-Eisen einstellt. Übliche Sinterstähle, die in der Regel Kohlenstoff enthalten, sintern im Bereich des γ-Eisens. Hierbei läuft die Sinterung 102 bis 103 mal langsamer ab als im α-Eisenbereich bei gleicher Temperatur. Werden beispielsweise Stahlpulver mit einem erhöhten Molybdängehalt gesintert, läuft die Sinterung bei Sintertemperaturen von zirka 1250°C im Bereich des α-Eisens ab. Hierbei ist nachteilig, da eine völlig kohlenstoffreine Sinterung stattfinden muß, daß bei einem anschließend erforderlich werdenden Einsatzhärten eine Kohlenstoffaufnahme in den Randbereichen des gesinterten Formkörpers nur schwer möglich ist und es zur Bildung eines spröden Karbidnetzes kommt.It is known to produce shaped bodies of any geometry from metallic powders, for example from steel powders, by sintering. The metallic powders are heat-treated at a certain temperature, which is slightly below the melting point of the sintered materials. As is known, the heat treatment of sintered steels results in areas with different lattice structures in which so-called α-iron, γ-iron or a mixed structure of α- and γ-iron is established. Common sintered steels, which usually contain carbon, sinter in the area of γ-iron. Here, the sintering 10 2 to 10 3 times slower than in the α-iron region at the same temperature. If, for example, steel powder with an increased molybdenum content is sintered, the sintering takes place at sintering temperatures of approximately 1250 ° C. in the area of the α-iron. The disadvantage here is that a completely carbon-free sintering must take place, that if a subsequent hardening becomes necessary, it is difficult to absorb carbon in the edge regions of the sintered shaped body and a brittle carbide network is formed.
Das erfindungsgemäße Verfahren mit den im Anspruch 1
genannten Merkmalen bietet demgegenüber den Vorteil, daß
höhermolybdänlegierte Sinterstähle einsatzgehärtet werden
können, ohne daß es zu einer Bildung von einem spröden
Karbidnetz kommt. Dadurch, daß die Sinterstähle nach dem
Sintern einer Wärmebehandlung unter Anwesenheit von
Kohlenstoff bei Temperaturen unterzogen werden, bei denen im
Sinterstahl ein Mindestanteil an γ-Eisen von 40 % vorliegt, ist es
vorteilhaft möglich, insbesondere in den Randbereichen des
Sinterstahls, eine derartige Gitterstruktur zu schaffen, die
anschließend zur Aufnahme von Kohlenstoff geeignet ist. Die
zusätzliche Wärmebehandlung wird unmittelbar anschließend an
das Sintern in einem Arbeitsschritt durchgeführt, wobei die
während des Sinterns vorhandene Schutzgasatmosphäre
beziehungsweise das Vakuum durch ein kohlenstoffabgebendes
Mittel, das heißt, Kohlenstoff enthaltende Atmosphäre,
ersetzt wird.The inventive method with the in
Beim erfindungsgemäßen Verfahren wird von der höheren Sintertemperatur auf den Temperaturbereich des Zwei-Phasen-Gebietes, heruntergekühlt, in dem ein Mindestanteil an γ-Eisen von 40 % vorliegt. Insofern ist das Vorhandensein eines Mindestanteils an γ-Eisen von 40 % für das Einsatzhärten von Sinterstählen notwendig. Würde von Raumtemperatur hochgeheißt, müßte die Zufuhr von Kohlenstoff während des Hochheizens gesperrt werden, weil auch unterhalb des Zwei-Phasen-Gebietes lediglich α-Eisen vorliegt (siehe Figur 2) und in diesem Bereich das schädliche Eisenkarbid entstehen würde. Folglich wäre eine lange Aufheizphase notwendig, die letztlich eine tote Prozeßzeit darstellt. Zur Vermeidung dieser Totzeit wird von der Sintertemperatur auf die Temperatur des Zwei-Phasen-Gebietes (α- und γ-Eisen) heruntergekühlt. Dadurch wird zugleich die beim Sintern zugeführte Wärmeenergie ausgenutzt.In the method according to the invention, the higher Sintering temperature to the temperature range of the two-phase area, cooled down in which a minimum proportion of γ-iron of 40% is present. In this respect, the presence of one Minimum proportion of γ iron of 40% for case hardening Sintered steels necessary. Would be from room temperature hoisted, the supply of carbon during the High heating can be blocked because it is also below the two-phase area only α-iron is present (see Figure 2) and the harmful iron carbide is created in this area would. As a result, a long heating-up phase would be necessary ultimately represents a dead process time. To avoid this dead time is from the sintering temperature to the Temperature of the two-phase area (α and γ iron) cooled down. This also makes the sintering process supplied thermal energy is used.
Wird die Wärmebehandlung vorzugsweise bei einer Temperatur von 1120°C durchgeführt, befinden sich 40 % des Werkstoffvolumens des höhermolybdänlegierten Sinterstahls in dem notwendigen Gitterstrukturbereich des γ-Eisens, wenn der Molybdän-Gehalt 3,5 Gew% beträgt. Hierdurch wird die anfängliche Aufnahme von Kohlenstoff begünstigt.The heat treatment is preferably at a temperature of 1120 ° C, 40% of the Material volume of the higher molybdenum alloyed sintered steel in the necessary lattice structure area of the γ-iron, if the Molybdenum content is 3.5% by weight. This will make the initial intake of carbon favors.
In bevorzugter Ausgestaltung der Erfindung ist vorgesehen, neben der zusätzlichen Wärmebehandlung nach dem Sintern anschließend die Einsatzhärtung bei den üblichen Einsatzhärtetemperaturen von 840 bis 950°C durchzuführen. Hierdurch wird erreicht, daß mittels der zwischen der Sinterung und der Einsatzhärtung durchgeführten zusätzlichen Wärmebehandlung eine Aktivierung des höhermolybdänlegierten Sinterstahls erfolgt, so daß das Einbauen von Kohlenstoff möglich wird, ohne daß es zur Bildung eines spröden Karbidnetzes kommt.In a preferred embodiment of the invention, in addition to the additional heat treatment after sintering then the case hardening in the usual Carry out case hardening temperatures of 840 to 950 ° C. This ensures that by means of between the Sintering and case hardening performed additional Heat treatment activates the higher molybdenum alloy Sintered steel takes place so that the installation of carbon becomes possible without it forming a brittle Carbide network is coming.
Weitere vorteilhafte Ausgestaltungen der Erfindung ergeben sich aus den übrigen in den Unteransprüchen genannten Merkmalen.Further advantageous embodiments of the invention result from the others mentioned in the subclaims Characteristics.
Die Erfindung wird nachfolgend in einem Ausführungsbeispiel anhand der zugehörigen Zeichnungen näher erläutert. Es zeigen: Figur 1 ein Blockdiagramm des Verfahrens zum Einsatzhärten von höhermolybdänlegierten Sinterstählen und Figur 2 ein Zustandsschaubild von molybdänlegierten Sinterstählen.The invention is described below in one embodiment explained in more detail with reference to the accompanying drawings. It 1 shows a block diagram of the method for Case hardening of higher molybdenum alloyed sintered steels and Figure 2 is a state diagram of molybdenum alloys Sintered steels.
Anhand des in Figur 1 dargestellten Flußdiagramms soll der
Ablauf des erfindungsgemäßen Verfahrens zum Einsatzhärten
von höhermolybdänlegierten Sinterstählen verdeutlicht
werden. In einem ersten Verfahrensschritt 10 wird der in
Pulverform vorliegende molybdänhaltige Stahl zu einem
Formkörper beliebiger geometrischer Gestalt verpreßt. Der
Molybdängehalt des Stahls beträgt beispielsweise 3,5 %. In
einem zweiten Verfahrensschritt 12 erfolgt anschließend die
Sinterung der zuvor gepreßten Formkörper bei einer
Sintertemperatur von 1250°C. Hierbei befindet sich das
Sintermaterial, wie anhand des in Figur 2 gezeigten
Zustandsschaubildes von molybdänhaltigen Sinterstählen nach
Höganäs verdeutlicht wird, ausschließlich im
Gitterstrukturbereich des α-Eisens. Die Sinterung erfolgt
unter einer Schutzgasatmosphäre, beispielsweise unter
Wasserstoff oder im Vakuum.Using the flow chart shown in Figure 1, the
Sequence of the case hardening method according to the invention
of higher molybdenum alloyed sintered steels
become. In a
In einem nächsten Verfahrensschritt 14 wird der zuvor
gesinterte höhermolybdänlegierte Sinterstahl einer weiteren
Wärmebehandlung bei einer Temperatur von beispielsweise
1120°C unterzogen. Diese Wärmebehandlung findet unter Zufuhr
von kohlenstoffhaltiger Atmosphäre statt. Dabei wird der
Sinterstahl zweckmäßigerweise von der Sintertemperatur
heruntergekühlt. Die Wärmebehandlung findet somit
unmittelbar nach dem Sintern statt.In a
Bei einer Temperatur von 1120°C befinden sich, wie wiederum
das Zustandsschaubild in Figur 2 verdeutlicht, 40 %
des Werkstoffvolumens des molybdänlegierten Sinterstahls im
Bereich des γ-Eisens. Hierdurch wird die Aufnahme von
Kohlenstoff aus der umgebenden Atmosphäre in die
Gitterstruktur des molybdänlegierten Sinterstahls
begünstigt. Die während des Verfahrensschrittes 14
durchgeführte Wärmebehandlung kann sehr vorteilhaft
beispielsweise gleich in dem Ofen durchgeführt werden, in
dem die Sinterung gemäß dem Verfahrensschritt 12
durchgeführt wird. Bei geringeren Anteilen an gelöstem
Kohlenstoff in dem molybdänlegierten Sinterstahl wandelt
sich bei der Temperatur von 1120°C, mit der die
Wärmebehandlung durchgeführt wird, auch das Restvolumen des
Werkstoffs in die Gitterstruktur des γ-Eisens um.At a temperature of 1120 ° C are, as again
the state diagram in Figure 2 clarifies, 40%
of the material volume of the molybdenum alloyed sintered steel in the
Area of γ-iron. This will make the inclusion of
Carbon from the surrounding atmosphere into the
Lattice structure of the molybdenum alloy sintered steel
favored. The
In einem nächsten Verfahrensschritt 18 erfolgt ein
Einsatzhärten des zuvor gesinterten und gemäß
Verfahrensschritt 14 wärmebehandelten höhermolybdänlegierten
Sinterstahls. Dieses Einsatzhärten erfolgt bei Temperaturen
von 840°C bis 950°C unter Zufuhr der kohlenstoffhaltigen
Atmosphäre oder anderer - hier nicht näher zu betrachtender
- kohlenstoffabgebender Mittel. Durch die zuvor
durchgeführte Wärmebehandlung gemäß Verfahrensschritt 14
erfolgte somit eine Aktivierung des molybdänlegierten
Sinterstahls, so daß durch die Einsatzhärtung in dem
Verfahrensschritt 18 auch unter den hier gegebenen
niedrigeren Temperaturen der Einbau von Kohlenstoff in die
Randzonen des Formkörpers möglich ist, ohne daß es zur
Bildung von einem spröden Karbidnetz kommt. Nach dem
Einsatzhärten im Verfahrensschritt 18 kann der insgesamt
erfindungsgemäß behandelte molybdänlegierte Sinterstahl
einer hier mit 16 bezeichneten speziellen
Verwendung zugeführt werden.A takes place in a next method step 18
Case hardening of the previously sintered and according
In der Figur 2 ist das bereits erwähnte Zustandsschaubild
von molybdänlegiertem Stahl gezeigt. Über den
Gewichtsprozenten GP des Molybdängehaltes in Prozent ist die
Temperatur T in °C aufgetragen. Anhand der eingetragenen
Trennlinien zwischen den sich in dem molybdänlegierten
Sinterstahl einstellenden Gitterstruktur bei
unterschiedlichen Temperaturen wird der α-Eisenbereich, der
γ-Eisenbereich und der zwischen diesen Bereichen liegende
Mischbereich aus γ- beziehungsweise α-Eisen verdeutlicht.
Beispielhaft ist ein Molybdängehalt von 3,5 % eingetragen,
wobei deutlich wird, daß bei einer Sintertemperatur von
1250°C, wie im Verfahrensschritt 12 zu Figur 1 erläutert,
sich der molybdänlegierte Sintrestahl ausschließlich in
seinem α-Eisen-Bereich befindet.The state diagram already mentioned is shown in FIG
of molybdenum alloy steel. On the
Weight percent GP of the molybdenum content in percent is the
Temperature T plotted in ° C. Based on the entered
Dividing lines between those in the molybdenum alloy
Sintered steel adjusting lattice structure
different temperatures, the α-iron range, the
γ-iron area and the area between these areas
Mixing area made of γ or α iron clarified.
A molybdenum content of 3.5% is entered as an example,
whereby it becomes clear that at a sintering temperature of
1250 ° C, as explained in
Claims (5)
- Process for case-hardening molybdenum-alloyed sintered steels with a relatively high molybdenum content of ≥ 2 per cent by weight, characterized in that the sintered steels are cooled immediately after the sintering to a temperature range in which the sintered steel contains at least 40% γ-iron, and in that in this temperature range the sintered steels are subjected to a heat treatment in the presence of carbon.
- Process according to Claim 1, characterized in that the heat treatment is carried out in a temperature range of from 1050°C to 1200°C, preferably 1120°C.
- Process according to Claim 1 or 2, characterized in that during the heat treatment the molybdenum-alloyed sintered steels are exposed to an agent which releases carbon.
- Process according to one of Claims 1 to 3, characterized in that the sintered steel has a molybdenum content of from 2 to 4% by weight, preferably of 3.5% by weight.
- Process according to one of the preceding claims, characterized in that the heat treatment is followed by the case-hardening at temperatures of from 840°C to 950°C.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE19520354A DE19520354C2 (en) | 1995-06-07 | 1995-06-07 | Process for case hardening of higher molybdenum alloyed sintered steels |
| DE19520354 | 1995-06-07 | ||
| PCT/DE1996/000916 WO1996041031A1 (en) | 1995-06-07 | 1996-05-25 | Process for case hardening higher molybdenum-alloyed sintered steels |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP0779937A1 EP0779937A1 (en) | 1997-06-25 |
| EP0779937B1 true EP0779937B1 (en) | 2001-09-26 |
Family
ID=7763575
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP96919584A Expired - Lifetime EP0779937B1 (en) | 1995-06-07 | 1996-05-25 | Process for case hardening higher molybdenum-alloyed sintered steels |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US5881356A (en) |
| EP (1) | EP0779937B1 (en) |
| JP (1) | JPH10504064A (en) |
| DE (2) | DE19520354C2 (en) |
| ES (1) | ES2164895T3 (en) |
| TW (1) | TW384312B (en) |
| WO (1) | WO1996041031A1 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE19714306C2 (en) * | 1997-03-24 | 1999-04-08 | Mannesmann Ag | Process for case hardening of sintered parts |
| JP3890401B2 (en) * | 2000-10-13 | 2007-03-07 | 独立行政法人物質・材料研究機構 | Separation of metal ions |
| CN110983090B (en) * | 2019-12-31 | 2021-07-13 | 金堆城钼业股份有限公司 | Sintering method of carbon-containing molybdenum alloy |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR1133499A (en) * | 1954-06-15 | 1957-03-27 | Federal Mogul Corp | Process Improvements for Making a Stainless Steel Article, Which Can Be Heat Treated |
| FR2015893A1 (en) * | 1968-08-19 | 1970-04-30 | Gen Motors Corp | Manufacture of iron article by processing powdered - iron |
| DE2053842A1 (en) * | 1969-11-04 | 1971-05-13 | Toyoda Chuo Kenkyusho Kk | Sinter bodies from iron and carbon powders - by two step heating process |
| US3658604A (en) * | 1969-12-29 | 1972-04-25 | Gen Electric | Method of making a high-speed tool steel |
| US3897618A (en) * | 1972-03-27 | 1975-08-05 | Int Nickel Co | Powder metallurgy forging |
| US3992763A (en) * | 1974-09-13 | 1976-11-23 | Federal-Mogul Corporation | Method of making powdered metal parts |
| US4018632A (en) * | 1976-03-12 | 1977-04-19 | Chrysler Corporation | Machinable powder metal parts |
| US4071382A (en) * | 1976-07-22 | 1978-01-31 | Midland-Ross Corporation | Method for case hardening powdered metal parts |
| GB2038882A (en) * | 1978-11-03 | 1980-07-30 | Davy Loewy Ltd | Carburising Sintered High Speed Steel |
| US4880461A (en) * | 1985-08-18 | 1989-11-14 | Hitachi Metals, Ltd. | Super hard high-speed tool steel |
| US4964980A (en) * | 1988-07-27 | 1990-10-23 | Amoco Corporation | Apparatus and process for stabilizing liquid hydrocarbon condensate |
| DE69117870T2 (en) * | 1990-10-31 | 1996-10-31 | Hitachi Metals Ltd | High speed steel made by sintering powder and process for producing it |
-
1995
- 1995-06-07 DE DE19520354A patent/DE19520354C2/en not_active Expired - Fee Related
-
1996
- 1996-05-25 EP EP96919584A patent/EP0779937B1/en not_active Expired - Lifetime
- 1996-05-25 WO PCT/DE1996/000916 patent/WO1996041031A1/en active IP Right Grant
- 1996-05-25 US US08/776,756 patent/US5881356A/en not_active Expired - Lifetime
- 1996-05-25 JP JP9500069A patent/JPH10504064A/en not_active Ceased
- 1996-05-25 ES ES96919584T patent/ES2164895T3/en not_active Expired - Lifetime
- 1996-05-25 DE DE59607766T patent/DE59607766D1/en not_active Expired - Lifetime
- 1996-06-07 TW TW085106846A patent/TW384312B/en not_active IP Right Cessation
Also Published As
| Publication number | Publication date |
|---|---|
| ES2164895T3 (en) | 2002-03-01 |
| DE59607766D1 (en) | 2001-10-31 |
| JPH10504064A (en) | 1998-04-14 |
| US5881356A (en) | 1999-03-09 |
| TW384312B (en) | 2000-03-11 |
| WO1996041031A1 (en) | 1996-12-19 |
| DE19520354C2 (en) | 1997-07-10 |
| DE19520354A1 (en) | 1996-12-12 |
| EP0779937A1 (en) | 1997-06-25 |
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