EP0105138B1 - Verfahren zum Sintern mit reduzierender Carbonisierung - Google Patents

Verfahren zum Sintern mit reduzierender Carbonisierung Download PDF

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Publication number
EP0105138B1
EP0105138B1 EP83107859A EP83107859A EP0105138B1 EP 0105138 B1 EP0105138 B1 EP 0105138B1 EP 83107859 A EP83107859 A EP 83107859A EP 83107859 A EP83107859 A EP 83107859A EP 0105138 B1 EP0105138 B1 EP 0105138B1
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Prior art keywords
zone
temperature
preform
carbon
carburizing
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Expired
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EP83107859A
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English (en)
French (fr)
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EP0105138A1 (de
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Larry Byrnes
Jon Gabrielsen
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Federal Mogul LLC
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Federal Mogul LLC
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Priority to AT83107859T priority Critical patent/ATE44983T1/de
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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
    • C23C8/08—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
    • C23C8/22—Carburising of ferrous surfaces
    • 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
    • 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
    • B22F3/24—After-treatment of workpieces or articles
    • 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

Definitions

  • This invention relates to a method for reducing, sintering and carburizing pre-alloyed, ferrous-base powder metal forging preforms.
  • pre-alloyed powder is cold pressed, sintered, and then forged.
  • oxides in the powder are reduced to acceptable levels.
  • This forging preform is lubricated, heated to an appropriate forging temperature, and forged to a close tolerance configuration. After forging, the part is normally quenched and stress relieved.
  • a number of powder metal parts require a post forging machining operation, such as grinding. In such cases, it is necessary to insurethatthe carbon case introduced during carburizing has adequate depth and composition to permit the removal of material during machining while maintaining the specified surface carbon content.
  • the carbon gradient produced by current powder metallurgy techniques has not been adequate for certain applications in which relatively high post-machining surface carbon is required.
  • U.S. Patent No. 3,992,763 discloses a method for simultaneously sintering and carburizing a pre- alloyed ferrous base powder metal forging preform, in a single furnace, single zone operation by maintaining the preform in a carburizing gas atmosphere for a period of time in the range of 20-40 minutes at a temperature from 2000 to 2100°F.
  • a diffusion step follows at a reduced temperature of from 1500 to 1750°F.
  • the object of this invention is to provide a method for making powder metal forging preforms of high strength ferrous-base alloys in which the times and temperatures for reducing, sintering carburizing such preforms are substantially reduced.
  • the present invention therefore provides a method for simultaneously sintering and carburizing a pre-alloyed, ferrous-base, powder metal forging preform of a type AISI 4600 series steel alloy having a base carbon content between 0.15 and 0.25 weight percent, and having a density of 6.2-6.8 gm/cm 3 , wherein said preform is preheated in the preheat zone of a continuous furnace, at a temperature which approaches the sintering/carburizing temperature for a period of time of time up to 10 minutes and no longerthan is required to burn off lubricants and to induce rapid heating of the preform in the hot zone of the furnace to a temperature up to 1066°C, simultaneously sintering and carburizing the preform in the hot zone of the furnace in a carburizing atmosphere and having a carbon content at a temperature substantially within the range of 843°C (1550°F) to 1066°C (1950°F) at the carbon potential of the atmosphere and for a period of time of 20 minutes to reduce oxides
  • cooling the preform in a first cooling zone of the furnace at a rate rapid enough to begin transformation of the austenitic phase in the thereby freezing the case carbon gradient, controlling the total time that the preform is at a temperature in the austenitic temperature range in all the aforesaid furnace zones to no more than 35 minutes and further cooling the preform in a second cooling zone of the furnace to a temperature below 260°C (500°F).
  • the invention involves an improved process for producing forging preforms, that is, a powder metal part which has been cold pressed, sintered, and carburized in preparation for the forging step.
  • the process produces a forging preform having an acceptable carbon gradient, but at times and temperatures substantially below those generally recognized as necessary to do so.
  • the invention is directed to hardenable alloy steels which contain one or more alloying additions of molybdenum, nickel, manganese, chromium and the like.
  • Carburized forging preforms have been produced by this process from pre-alloyed powder similar in composition to the AISI 4600 series steel at temperatures below 1093°C (2000°F) with a total time above the austenitic formation temperature of about 35 minutes or less.
  • this process is capable of reducing oxides to acceptable levels, that is, less than 1,000 ppm 0 2 .
  • current sintering/carburizing process for comparable alloys which are conducted at 1121°C (2050°F) and with times above austenitic temperatures of approximately 60 minutes. Consequently, the cost of producing forging preforms is substantially reduced because production time is substantially reduced and energy requirements are reduced.
  • the process includes a step for modifying the carbon gradient to produce an improved forging preform for applications which require a relatively high surface carbon content after machining.
  • the carbon gradient is modified to produce a plateau having a depth of at least 0.025 cm. (0.010 inches) over which the carbon content decreases by no more than about 0.10%. (Compositions are given throughout in weight percent.)
  • This carbon gradient permits the removal of up to about 0.025 cm. (0.010 inches) of stock during machining without reducing the surface carbon content below an acceptable level.
  • This feature of the invention appears to be particularly important in the production of races for rolling contact bearings from powder metal since these races have ground surfaces which require relatively high postgrinding surface hardness.
  • the sintering/carburizing process according to the invention is conducted in a fairly conventional belt-type sintering furnace which includes a preheat zone, a hot zone, and a cooling zone. Sintering and carburizing are performed simultaneously in the hot zone. A short diffusion zone may be added immediately following the hot zone when it is desired to modify the carbon gradient from that which is obtained during primary carburization in the hot zone.
  • the cold pressed preform is heated to burn off lubricants, such as zinc stearate, stearic acid, and waxes, the conventional function of the preheat zone.
  • lubricants such as zinc stearate, stearic acid, and waxes
  • the preheat zone is maintained at a temperature significantly higher than usual to rapidly heat the preform to a predetermined sintering/carburizing temperature. More specifically, while the preheat zone in conventional practice is typically heated to temperatures up to 816°C (1500°F), temperatures as high as 1093°C (2000°F) could be employed in accordance with this invention. It should be noted, however, that the temperature of the preheat zone is determined in light of the process temperature. Hence, if the sintering/carburizing temperature is lowered to 954°C (1750°F), the temperature in the preheat zone would also be lowered. The time in the preheat zone is also reduced. While conventional sintering practice specifies a time in the preheat zone of about 15 to 30 minutes, the time in the preheat zone according to the instant invention may be 10 minutes or less.
  • the preform moves into the hot zone in which it is simultaneously sintered and carburized.
  • the hot zone is maintained at. a temperature below 1093°C (2000°F) which is at least 27°C (50°F) below temperatures normally recommended for prealloyed powders of this type.
  • An atmosphere having a high carbon potential is used in the hot zone, that is, an atmosphere having a carbon potential which is higher than the desired surface carbon content.
  • the preform is maintained in the hot zone for approximately 20 minutes.
  • the preform is moved from the hot zone into a first cooling zone in which the preform is rapidly cooled (within approximately five minutes) to begin the austenitic to martensitic transformation to freeze the case carbon gradient obtained during carburization.
  • the preform is then cooled in a second cooling zone to a temperature below about 260°C (500°F) to prevent detrimental oxidation.
  • the preform is moved from the hot zone into a diffusion zone for modifying the shape of the carbon gradient obtained in the hot zone.
  • the diffusion zone is heated by the product moving through the zone so that the temperature upon entry is approximately equal to the temperature of the hot zone.
  • the diffusion zone is insulated so that the temperature of the preform does not fall below the austenitic transformation temperature.
  • a carburizing atmosphere of a desired carbon potential is maintained in the diffusion zone. The atmosphere is controlled independently from the atmosphere in the sintering/carburizing zone and has a carbon potential which is below the carbon potential of the hot zone and is at, or slightly below, the desired surface carbon content of the preform.
  • the preform is maintained in the diffusion zone for up to about five minutes to change the carbon gradient to one with a plateau which extends to a depth of at least 0.025 cm. (0.010 inches) with no more than about a 0.10% decrease in carbon content.
  • the preform is then rapidly cooled in the first cooling zone to begin the austenitic to martensitic transformation and thereby freeze the carbon gradient in the case. Thereafter, the preform is moved through the second cooling zone under conditions similar to those described with respect to the first embodiment.
  • Time and temperature are considered to be inversely related with respect to sintering and carburizing processes. That is, if the temperature is reduced, the time must be increased, and vice versa.
  • the diffusion rate of carbon in the powder metal preform does not increase, but is fairly constant over the temperature range 843°C to 1066°C (1550°F to 1950°F). Moreover, and more significantly, the diffusion rate is substantially higher in the powder metal preform over this temperature range than the diffusion rate in wrought material. At temperatures above 1066°C (1950°F) the rate of diffusion begins increasing rapidly and beyond 1093°C (2000°F) the rates of diffusion become approximately equal for both materials so that advantage attained at lower temperatures is lost. Therefore, the instant invention is designed to operate over the temperature range of about 843°C to about 1066°C (about 1550°F to about 1950°F).
  • Figure 1 shows the rate of diffusion of carbon in powder metal and wrought material as a function of temperature. While the rate of diffusion in wrought material is very dependent on temperature, as is expected, the rate of diffusion in powder metal is nearly insensitive to temperature over the temperature range 843°C-1066°C (1550°F-1950°F).
  • the diffusion rate in the powder metal preform is substantially higher over this temperature range than in the wrought material. Above 1066°C (1950°C) the rate of diffusion in powder metal seems to behave similarly to that in wrought material.
  • oxide levels Due to recent improvements in the manufacture of ferrous-base, pre-alloyed powders, oxide levels have been substantially reduced. If such improvements continue, it is quite likely that the oxide level can be reduced below the maximum level specified for forged powder metal parts, that is, below 1000 ppm 0 2 . When this occurs, the reduction of oxides can also be ignored. In the meantime, a temperature is selected which, in conjunction with a reducing atmosphere, is capable of reducing oxides to the required levels. For example, at 1010°C (1850°F) the oxides in the powder can be reduced to a level of about 900 ppm O2 which is below the specified maximum. Time at temperature can also be shortened due to the improved powders which have lower oxide contents to begin with.
  • the furnace employed in carrying out the process is, for the most part, a conventional, belt-type, continuous furnace typical of those used in the powder metal parts industry. Special modifications and features will be apparent from the more detailed description of the furnace which follows.
  • the furnace is divided into four functional zones. With reference to the schematic shown in Figure 4, these comprise a preheat zone 10, a sinter/carburize zone 12, a first cooling zone 14 and a second cooling zone 16.
  • the furnace may be heated electrically or with gas and the work is moved through it on a continuous mesh belt.
  • the furnace also has the necessary plumbing for maintaining a desired carburizing atmosphere in the sinter/carburize zone 12. Other features of the furnace will be described in connection with the description of the process.
  • Pre-alloyed ferrous-base powder metal is first cold pressed into green forging preforms having a shape generally similar to the final forged part. This is done according to standard powder metallurgy practice and will not be described in greater detail.
  • the pre-alloyed powder is one of the high strength ferrous-base alloys similar to AISI 4600 series with a predetermined base carbon content generally between 0.15 and 0.25% carbon. As previously noted, these powders include alloy additions which are believed to require high temperatures and relatively long process times. Preferably, the powder has the lowest oxide content economically attainable, currently 1500-2500 ppm 0 2 .
  • the cold-pressed briquette typically has a density of 6.2-6.8 g/ c m3 .
  • the green forging preforms are loaded onto the charge end of the furnace and are conveyed into the preheat zone 10.
  • waxes and lubricants are burned out of the green preform.
  • the preform is heated rapidly to a temperature which at least approaches the sintering/carburizing temperature. For example, if a sintering/carburizing temperature of 1066°C (1950°F) is selected, the preheat zone is heated to at least 1010°C (1850°F) so that the temperature of the gree preform is near this temperature by the time it traverses the preheat zone.
  • a belt speed of at least 30.5 cm (12 inches) per minute is maintained so that each green preform resides in the preheat zone for a period no longer than about 10 minutes.
  • the forging preform is moved into the sinter/carburize zone 12.
  • This zone is referred to as the "hot" zone in convention sintering furnaces.
  • the preform is sintered, carburized and reduced.
  • a carburizing atmosphere for example, an endothermic gas, is maintained at a carbon potential which is greater than the desired surface carbon content. It should be recognized, however, that other carburizing atmospheres can be used. For example, if a surface carbon content of 0.85%-1.00%C is required, a carbon potential of up to the saturation level of carbon in austenite at the specified temperature is maintained in the sinter/carburize zone; e.g. approximately 1.9% at 1066°C (1950°F).
  • the carbon potential of the atmosphere can be controlled in a number of known manners including, for example, maintaining a constant analyzed methane level in the zone using infrared analyzers. Since sintering furnaces vary in design and operating characteristics, it may be necessary empirically to correlate methane level and carbon potential, however, once the relationship is established, it is quite easy to maintain the desired methane level using standard control equipment.
  • the temperature of the sinter/carburize zone 12 is maintained at a temperature below 1066°C (1950°F), the upper limit.
  • the lower limit for the temperature has been determined in light of two main considerations: the sintered preform strength and the ability to reduce oxides to acceptable levels. Due to the oxide levels of currently available powders, the ability to reduce oxides is the more restrictive consideration. If a temperature of 1066° (1950°F) is selected to insure oxide reduction well below 1000 ppm O2, preforms with adequate strength for subsequent forging are produced. However, as the oxide content of the powder is reduced in the starting powder, the preform strength limits will ultimately control the lower limit for temperature. In any event from our studies we conclude that the optimum temperature range for the process is from about 843°C-1066°C (15500-1950°F).
  • the time period during which the forging preform resides in the sintering/carburizing zone is short compared to recognized practice. Since the belt speed is at least 30.5 cm. (12 inches) per minute, the period of time in this zone is no longer than 20 minutes.
  • a case carbon gradient is produced in the forging preform having a surface carbon content which is below the carbon potential of the atmosphere, but approximately equal to the desired surface carbon content.
  • the carbon content decreases relatively constantly with distance from the surface to a depth of at least 0.050 cm. (0.020 inches) after which the carbon content falls off less rapidly and non-linearly to the core carbon content.
  • Curve A in Figure 2 is characteristic of this shape of the carbon gradient produced in the sintering/carburizing zone.
  • the preform is sintered. Although sintering is time and temperature dependent, it has been found that adequate strength can be imparted under the conditions described to produce an acceptable forging preform.
  • the preform After the sinter/carburize zone, the preform is moved into a first cooling zone 14 in which it is rapidly cooled to begin the austenitic to martensitic transformation to fix, or freeze, the carbon gradient obtained in the hot zone.
  • the temperature in the carbon case of the preform must be reduced to a temperature below the austenitic to martensitic transformation temperature within a period of no longer than approximately five minutes. This is achieved by providing a water jacket around the first cooling section. At a belt speed of 30.5 cm. (12 inches) per minute, the water jacket provides enough cooling to reduce the temperature below the austenitic transformation temperature within the first five feet of this section.
  • the atmosphere is not separately controlled, but consists of the atmosphere which flows from the sinter/carburize zone.
  • the forging preform is moved into a second cooling zone 16.
  • the second cooling zone 16 comprises successively the remainder of the water jacketed section, a forced circulation section and another water jacketed section.
  • the preform is gradually cooled to a temperature below about 260°C (500°F). If the forging preform is exposed to an oxidizing atmosphere at a temperature above about 260°C (500°F), unacceptable oxidation and scaling will occur.
  • a diffusion zone 22 is added between the sinter/carburize zone 20 and the first cooling zone 24.
  • the remainder of the furnace is the same as the one described with respect to the first embodiment, that is, it also includes a preheat zone 18 and a second cooling zone 26.
  • the manner in which the preforms are processed is also the same through the sinter/ carburize zone so the description will not be repeated.
  • the diffusion zone 22 is used to modify the carbon gradient obtained in the sintering/ carburizing zone 20 by forming a plateau which extends to a depth of at least 0.025 cm. (0.010 inches). This plateau produces a case of high carbon which is deep enough to permit surface grinding to a depth of 0.025 cm. (0.010 inches) while maintaining the required surface carbon content, and, hence, the required surface hardness.
  • the diffusion zone 22 comprises a furnace section which is insulated to prevent heat loss. It is similar in construction to the buffer zone commonly used in sintering furnace design. However, unlike conventional sintering furnace design, the diffusion zone includes means for controlling the atmosphere. The atmosphere in the diffusion zone is controlled to produce a carbon potential at or slightly below the desired surface carbon content. Typically, the carbon potential of the atmosphere in the diffusion zone is lower than the carbon potential of the atmosphere in the sintering/carburizing zone. In test conducted using forging preforms made of a pre- alloyed powder similar to AISI 4618 alloy steel, the carbon potential of the sinter/carburize zone was established to produce a surface carbon content of over 1.2% carbon. The atmosphere in the diffusion zone 22 was controlled to produce a final carbon content at the surface of between 1.00% and 1.10% carbon.
  • Figure 3 is a graph showing carbon content as a function of depth in a preform.
  • Curve A is typical of the carbon gradient produced in the sinter/ carburize zone of the furnace. That is, the carbon content decreases relatively constantly to a depth of approximately 0.050 cm. (0.020 inches) from the surface of the preform after which the carbon content decreases nonlinearly toward the core carbon content.
  • the carbon gradient is modified to produce a plateau having at the surface of the preform the desired carbon content and extending to a depth of approximately 0.025 cm. (0.010 inches) with no more than about a ten point (0.1%) decrease in carbon content.
  • Atypical carbon gradient produced in the diffusion zone is illustrated by Curve B of Figure 3. This carbon gradient profile is more acceptable for certain forged parts which must be machined, e.g., ground after forging.
  • the preform After moving through the diffusion zone 22, the preform enters the first cooling zone 24 in which at least the carbon case is cooled to a temperature below the austenitic transformation temperature within a period of no longer than above five minutes to freeze the case carbon gradient. The preform is then further cooled in the second cooling zone 26 for a period of twenty to twenty- five minutes to a temperature below about 260°C (500°F).
  • the invention provides a significantly improved process for producing powder metal forging preforms.
  • the invention permits such preforms to be produced at times and temperatures substantially below those currently employed and, therefore, reduces the cost of production.
  • an improved carbon gradient is produced in the preform which facilitates subsequent machining of the preform.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Forging (AREA)

Claims (4)

1. Verfahren zum gleichzeitigen Sintern und Aufkohlen eines vorlegierten Pulvermetallschmiedestücks auf Eisenbasis aus einer Strahllegierung von Typ AISI 4600 mit einem Ausgangskohlenstoffgehalt zwischen 0,15 und 0.25 Gew.% und einer Dichte von 6,2 bis 6,8 g/cm3, in dem der Vorformling in der Vorerhitzungszone eines Durchlaufofens auf einer der Sinter- und Aufkohltemperatur angenäherten Temperatur während eines Zeitraums gehalten wird, der bis zu 10 min beträgt, aber nicht länger ist, als es zum Abbrennen von Schmierstoffen und zum schnellen Erhitzen des Vorformlings in der heißen Zone des Ofens auf eine Temperatur von bis zu 1066°C erforderlich ist, der Vorformling in der heißen Zone des Ofens in einer Kohlenstoff enthaltenden Aufkohlatmosphäre, die sich auf einer Temperatur im wesentlichen im Bereich von 843 bis 1066°C befindet während eines Zeitraums von 20 min gleichzeitig gesintert wird, so daß Oxide reduziert werden und in der Randzone des Vorformlings ein Kohlenstoffgradient hergestellt wird, der von einem annähernd dem gewünschten Randkohlenstoffgehalt entsprechenden Oberflächenkohlenstoffgehalt bis zu einer Tiefe von 0,056 cm relativ konstant abnimmt, worauf der Vorformling in einer ersten Kühlzone des Ofens so schnell abgekühlt wird, daß die Umwandlung der Austenitphase eingeleitet und dadurch der Kohlenstoffgradient in der Randzone eingefroren wird, die Dauer der Zeit, in der sich der Vorformling in allen vorgenannten Zonen des Ofens auf einer Temperatur im Austenittemperaturbereich befindet, auf nicht mehr als 35 min begrenzt wird, und der Vorformling in einer zweiten Kühlzone des Ofens auf eine Temperatur unter 260°C abgekühlt wird.
2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, daß der Verformling in der ersten Kühlzone etwa fünf Minuten lang abgekühlt wird.
3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, daß die Atmosphäre in der heißen Zone zwangs-umgewälzt wird.
4. Verfahren nach Anspruch 1, 2 oder 3, dadurch gekennzeichnet, daß in einer der heißen Zone folgenden und der ersten Zone vorhergehenden Diffusionszone der Kohlenstoffgehalt modifiziert wird, wobei die Temperatur am Eintritt der Diffusionszone der Temperatur in der heißen Zone entspricht und mit zunehmendem Abstand von der heißen zone auf eine Temperatur abnimmt, die nicht niedriger ist als die Austenittemperatur in einer Aufkohlatmosphäre mit einem Kohlenstoffpotential, das dem gewünschten Oberflächenkohlenstoffgehalt entspricht oder niedriger ist als dieser, und die Verweilzeit in der Diffusionszone so lang ist, daß schließlich in der Randzone ein Kohlenstoffgradient mit einem Kohlenstoffplateau erhalten wird, in dem an der Oberfläche des Vorformlings der gewünschte Kohlenstoffgehalt vorhanden ist und in dem bis zu einer Tiefe von 0,025 cm der Kohlenstoffgehalt um nicht mehr als zehn Punkte (0,10%) abnimmt.
EP83107859A 1982-08-09 1983-08-09 Verfahren zum Sintern mit reduzierender Carbonisierung Expired EP0105138B1 (de)

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AT83107859T ATE44983T1 (de) 1982-08-09 1983-08-09 Verfahren zum sintern mit reduzierender carbonisierung.

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US40665882A 1982-08-09 1982-08-09
US406658 1982-08-09

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EP0105138A1 EP0105138A1 (de) 1984-04-11
EP0105138B1 true EP0105138B1 (de) 1989-07-26

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EP (1) EP0105138B1 (de)
JP (1) JPS59133301A (de)
AT (1) ATE44983T1 (de)
CA (1) CA1225536A (de)
DE (1) DE3380264D1 (de)
MX (1) MX156818A (de)

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3448789B2 (ja) * 1995-01-20 2003-09-22 同和鉱業株式会社 ガス浸炭方法
SE9701976D0 (sv) * 1997-05-27 1997-05-27 Hoeganaes Ab Method of monitoring and controlling the composition of the sintering atmosphere
US7431777B1 (en) 2003-05-20 2008-10-07 Exxonmobil Research And Engineering Company Composition gradient cermets and reactive heat treatment process for preparing same
AT505699B1 (de) 2007-09-03 2010-10-15 Miba Sinter Austria Gmbh Verfahren zur herstellung eines sintergehärteten bauteils
EP3043135A1 (de) * 2015-01-08 2016-07-13 Linde Aktiengesellschaft Vorrichtung und Verfahren zur Steuerung eines Sinterprozesses
US11007572B2 (en) 2015-08-17 2021-05-18 Ntn Corporation Sliding member and method for producing same
CN108296480B (zh) * 2018-03-23 2020-01-31 厦门理工学院 一种高纯难熔金属块体的制备方法

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB665794A (en) * 1949-09-27 1952-01-30 Isthmian Metals Inc Powder metallurgy process for producing steel parts
US3992763A (en) * 1974-09-13 1976-11-23 Federal-Mogul Corporation Method of making powdered metal parts
JPS5179606A (en) * 1974-11-09 1976-07-12 Toyo Kogyo Co Kotansotetsukeishudobuzaino shoketsuhoho
GB2007719B (en) * 1977-11-15 1982-03-31 British Steel Corp Production of metal compacts

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DE3380264D1 (en) 1989-08-31
CA1225536A (en) 1987-08-18
JPH0211644B2 (de) 1990-03-15
JPS59133301A (ja) 1984-07-31
ATE44983T1 (de) 1989-08-15
MX156818A (es) 1988-10-05
EP0105138A1 (de) 1984-04-11

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