DE4204982A1 - Thermochemical-thermal treatment of case hardening steels - with deep cooling between hardening and tempering - Google Patents
Thermochemical-thermal treatment of case hardening steels - with deep cooling between hardening and temperingInfo
- Publication number
- DE4204982A1 DE4204982A1 DE19924204982 DE4204982A DE4204982A1 DE 4204982 A1 DE4204982 A1 DE 4204982A1 DE 19924204982 DE19924204982 DE 19924204982 DE 4204982 A DE4204982 A DE 4204982A DE 4204982 A1 DE4204982 A1 DE 4204982A1
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- Germany
- Prior art keywords
- hardening
- temperature
- tempering
- thermochemical
- carburization
- 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.)
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Classifications
-
- 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
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/04—Hardening by cooling below 0 degrees Celsius
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Heat Treatment Of Articles (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
Die Erfindung betrifft ein Verfahren zur thermochemisch-thermischen Behandlung von Einsatzstählen, welches eine Einsatzhärtung oder Carbo nitrierung bei einer Temperatur oberhalb des AC 3-Punktes des Kern werkstoffes, die mit einer Aufkohlung oder einer Aufkohlung mit Auf stickung der Randzone verbunden ist, einen Härteprozeß mit an schließender Abschreckung und einen Anlaßvorgang umfaßt.The invention relates to a method for thermochemical-thermal treatment of case-hardening steels, which case-hardening or carbon nitriding at a temperature above the AC 3 point of the core material, which is associated with a carburization or a carburization with embroidery on the edge zone, with a hardening process at closing deterrent and starting process.
Aus der GB-OS 22 09 058 ist ein derartiges Behandlungsverfahren für Einsatzstähle bekannt, mit dem die Resistenz des Werkstoffs von Wälz lagerbauteilen gegen Wälzermüdung bei ungünstigen Schmierbedingungen, insbesondere bei verschmutzten Schmierstoffen, verbessert wird.GB-OS 22 09 058 describes such a treatment method for Case hardening steels known, with which the resistance of the material of rolling bearing components against rolling fatigue in unfavorable lubrication conditions, especially with dirty lubricants, is improved.
Dieses Verfahren sieht vor, daß zunächst eine reine Aufkohlung der Randzone auf einen C-Gehalt von 0,7 bis 1,1% C bei einer Temperatur von 930°C erfolgt. Im Anschluß an die darauffolgende Abkühlung auf Raumtemperatur wird eine zweite Wärmebehandlung bei einer Temperatur von 830°C bis 870°C durchgeführt, die mit einer Nitrierung bzw. Carbo nitrierung kombiniert ist. Nach dem anschließenden Abschrecken auf Raumtemperatur werden die Bauteile bei einer Temperatur von 160°C und einer Haltedauer von zwei Stunden angelassen.This procedure provides that initially a pure carburization of the Edge zone to a C content of 0.7 to 1.1% C at a temperature of 930 ° C. Following the subsequent cooling Room temperature is a second heat treatment at one temperature from 830 ° C to 870 ° C carried out with a nitration or carbo nitriding is combined. After quenching afterwards The components are at room temperature at a temperature of 160 ° C and tempered for two hours.
Das entstehende Gefüge weist dann in der Randzone einen Austenitgehalt von 20 bis 45 Vol.-% und einen Carbid- oder Nitridgehalt von 3 bis 15 Vol.-% auf. The resulting structure then has an austenite content in the edge zone from 20 to 45% by volume and a carbide or nitride content from 3 to 15 % By volume.
Die nach diesem Verfahren behandelten Wälzlagerteile weisen tatsäch lich verbesserte Eigenschaften hinsichtlich der Wälzermüdung und der Verschleißfestigkeit auf, die jedoch für hochbeanspruchte Bauteile wie z. B. Tassenstößel im Ventiltrieb von Brennkraftmaschinen wegen des hohen Restaustenitanteils nicht ausreichen. Darüberhinaus erfordert das Verfahren unter anderem eine sehr lange Haltezeit bei der zweiten Wärmebehandlungsstufe, so daß die Durchführung des Verfahrens mit erheblichen Kosten verbunden ist.The roller bearing parts treated according to this procedure actually have Lich improved properties in terms of rolling fatigue and Wear resistance, which, however, for highly stressed components such as e.g. B. tappet in the valve train of internal combustion engines because of high levels of austenite are not sufficient. Furthermore requires the process includes a very long hold time at the second Heat treatment stage, so that the implementation of the process with considerable costs.
Aufgabe der vorliegenden Erfindung ist es, ein thermochemisch-ther misches Behandlungsverfahren vorzuschlagen, das wirtschaftlich durch führbar ist und die Verschleißfestigkeit hochbeanspruchter Bauteile auch bei ungünstigen Schmierbedingungen verbessert.The object of the present invention is a thermochemical ther propose a mixed treatment process that is economically viable is feasible and the wear resistance of highly stressed components improved even under unfavorable lubrication conditions.
Diese Aufgabe wird dadurch gelöst, daß das Verfahren folgende Ver fahrensschritte in der angegebenen Reihenfolge umfaßt:This object is achieved in that the method Ver Driving steps in the order given include:
- - Eine Einsatzhärtung oder Carbonitrierung bei einer Temperatur von 900 bis 1050°C, wobei eine übereutektoide Aufkohlung oder eine übereutektoide Aufkohlung mit Aufstickung der Randzone erfolgt, und der Kohlenstoffgehalt bzw. Kohlenstoff- und Stickstoffgehalt in der Randzone größer als 1 Gew.-% aber kleiner als die durch die S-E-Linie im Zustandsdiagramm des Werkstoffs in Abhängigkeit von der Temperatur definierte maximale Löslichkeit des Kohlenstoffs im Austenit ist;- Case hardening or carbonitriding at a temperature of 900 to 1050 ° C, a hypereutectoid carburization or hypereutectoid carburization occurs with embroidery of the peripheral zone, and the carbon content or carbon and nitrogen content in the peripheral zone greater than 1 wt .-% but smaller than that by S-E line in the state diagram of the material depending on the temperature defined maximum solubility of the carbon is in austenite;
- - eine Abkühlung auf einen Wert unterhalb des Ar1-Punktes mit einer Abschreckgeschwindigkeit, bei der eine Korngrenzenzementitaus scheidung vermieden ist;cooling to a value below the A r1 point with a quenching rate at which a grain boundary cementite separation is avoided;
- - einen Härteprozeß mit einer Aufheizgeschwindigkeit von 20 bis 80°C/Minute, einer Temperatur von 770 bis 830°C und einer Halte dauer von 5 bis 15 Minuten.- A hardening process with a heating rate of 20 to 80 ° C / minute, a temperature of 770 to 830 ° C and a hold takes 5 to 15 minutes.
Durch die hohen Temperaturen während der Aufkohlung bzw. Carbonitrie rung von 900 bis 1050°C wird die Haltezeit erheblich verringert. Sie sind gleichzeitig Voraussetzung, daß im Austenit ein hohes Lösungsver mögen für Kohlenstoff und Stickstoff vorliegt und mithin ein Kohlen stoffgehalt von mehr als 1 Gew.-% in der Randzone erreicht werden kann. Das Kohlenstoff- und Stickstoffpotential in der Atmosphäre ist während dieser Phase allerdings auf die maximale Löslichkeit von Kohlenstoff und Stickstoff im Austenit abzustimmen. Diese Löslichkeit ergibt sich auf der S-E-Linie im Eisenkohlenstoff-Diagramm. Überschreitet das Kohlenstoffpotential in der Atmosphäre nämlich die maximale Löslich keit von Kohlenstoff im Austenit erfolgt eine Überkohlung, mit der Folge, daß Korngrenzenzementit ausgeschieden wird. Die Haltezeit während des Einsetzens bzw. Carbonitrierens bestimmt sich im konkreten Fall nach der geforderten Einhärtetiefe.Due to the high temperatures during carburization or carbonitrie The holding time is considerably reduced at temperatures between 900 and 1050 ° C. they are at the same time a prerequisite that a high solution ver may exist for carbon and nitrogen and therefore carbon substance content of more than 1 wt .-% can be achieved in the peripheral zone. The carbon and nitrogen potential in the atmosphere is during this phase, however, on the maximum solubility of carbon and tune nitrogen in austenite. This solubility arises on the S-E line in the iron-carbon diagram. Exceeds that Carbon potential in the atmosphere namely the maximum soluble Carbon in austenite causes overcarburization with which Consequence that grain boundary cementite is excreted. The hold time during the insertion or carbonitriding is determined specifically Case after the required hardening depth.
Nach dem Einsatzhärten oder Carbonitrieren erfolgt eine schnelle Unterkühlung des Gefüges durch Abschrecken auf Raumtemperatur. Damit wird die Zementitausscheidung an den Austenitkorngrenzen unterdrückt und es entsteht ein Gefüge aus Martensit und hohem Restaustenitanteil von 40 bis 90 Vol.-%. Eine direkte Unterkühlung im Ofen mit anschlie ßender isothermer Umwandlung bei Temperaturen unter dem Ac1-Punkt ist ebenfalls möglich.After case hardening or carbonitriding, the structure is rapidly supercooled by quenching to room temperature. This suppresses the precipitation of cementite at the austenite grain boundaries and a structure of martensite and a high proportion of austenite of 40 to 90% by volume is formed. Direct subcooling in the furnace with subsequent isothermal conversion at temperatures below the A c1 point is also possible.
Dieser ersten Behandlungsstufe schließt sich eine zweite Wärmebehand lung an, bei der der Werkstoff auf eine Temperatur zwischen 770 und 830°C, vorzugsweise 790 bis 810°C, mit einer für Durchlaufhärteöfen typischen Aufheizgeschwindigkeit von 20 bis 80°C pro Minute und einer Haltezeit zwischen 5 und 15 Minuten an, der dann eine übliche Ölab schreckung folgt. Durch diese zweite Wärmebehandlung wird erreicht, daß sich bei der geregelten Erwärmung auf die Austenitisierungstempe ratur der hohe Anteil gelöster Stickstoff- und Kohlenstoffatome in Form feinstdisperser Karbide und Carbonitride gleichmäßig fein ver teilt, innerhalb der Kristalle ausscheidet. Da bei der niedrigen zweiten Wärmebehandlungstemperatur das Lösungsvermögen des Austenits für Kohlenstoff deutlich niedriger liegt als bei der ersten hohen Behandlungstemperatur, wird ein Teil der ausgeschiedenen Karbide bzw. Carbonitride im Austenit nicht gelöst. Die Austenitisierung selbst, das heißt die Haltezeit auf der Austenitisierungstemperatur, darf dagegen nur kurzzeitig erfolgen, um eine Karbidvergrößerung zu ver meiden. Nach der anschließenden martensitischen Abschreckung, die durch die Ölabschreckung erreicht wird, liegt ein Gefüge vor, das neben feinst nadeligem Martensit einen Restaustenitanteil von 25 bis 40% und zahlreiche, feinste Karbide mit einem Flächenanteil zwischen 8 und 25% aufweist. Außerdem zeigt das Gefüge eine sehr feine Bruch korngröße.This first treatment stage is followed by a second heat treatment at which the material reaches a temperature between 770 and 830 ° C, preferably 790 to 810 ° C, with one for continuous hardening furnaces typical heating rate of 20 to 80 ° C per minute and one Hold time between 5 and 15 minutes, which is then a common oil drain horror follows. This second heat treatment achieves that in the controlled heating to the austenitizing temp rature the high proportion of dissolved nitrogen and carbon atoms in Form finely dispersed carbides and carbonitrides evenly fine ver divides, excretes within the crystals. Because at the low second heat treatment temperature the dissolving power of the austenite for carbon is significantly lower than the first high Treatment temperature, a part of the excreted carbides or Carbonitrides not dissolved in austenite. The austenitization itself, that is, the holding time at the austenitizing temperature on the other hand, only take a short time to increase the carbide avoid. After the subsequent martensitic deterrence, the is achieved by oil quenching, there is a structure that in addition to the finest acicular martensite, a residual austenite content of 25 to 40% and numerous, finest carbides with an area share between 8 and 25%. In addition, the structure shows a very fine break grain size.
Diesem zweiten Behandlungsschritt kann sich dann direkt ein Anlassen bei 160 bis 180°C und zwei Stunden Haltedauer anschließen. Eine höhere Anlaßtemperatur bis 300°C ergibt noch eine hinreichend hohe Härte von mindestens 58 HRC.This second treatment step can then be started directly Connect at 160 to 180 ° C and a holding time of two hours. A higher one Tempering temperature up to 300 ° C results in a sufficiently high hardness of at least 58 HRC.
Bei einem bevorzugten erfindungsgemäßen Verfahren ist jedoch vorgese hen, vor dem Anlassen eine Tiefkühlbehandlung bis -120°C durchzufüh ren, bei der der Restaustenitanteil im Gefüge auf 5 bis 20% abgesenkt wird.In a preferred method according to the invention, however, is provided prior to starting, freeze treatment to -120 ° C in which the residual austenite content in the structure is reduced to 5 to 20% becomes.
Durch das erfindungsgemäße Verfahren zur thermochemisch-thermischen Behandlung werden dem Werkstoff Eigenschaften wie eine hohe Ver schleißfestigkeit und eine hohe Zähigkeit verliehen.The inventive method for thermochemical-thermal Treatment will give the material properties such as a high ver wear resistance and high toughness.
Ein nach dem Verfahren behandelter Einsatzstahl zeichnet sich dadurch aus, daß das Gefüge in der Randzone feinstdisperse, intrakristalline Karbidausscheidungen mit einem Flächenanteil größer 8% und eine Bruchkorngröße feiner 10 nach Jernkontoret Bruchprobensatz bzw. Korn größe nach ASTM E112 feiner 10 aufweist.A case-hardened steel treated according to the process is characterized by this from that the structure in the marginal zone is finely dispersed, intracrystalline Carbide precipitates with a surface area greater than 8% and one Fracture grain size finer 10 according to Jernkontoret fracture sample set or grain according to ASTM E112 finer 10.
Die einzige Figur zeigt schematisch das erfindungsgemäße Verfahren zur thermochemisch-thermischen Behandlung von Einsatzstahl. In der mit 1 bezeichneten Phase erfolgt die Carbonitrierung oder Einsatzhärtung bei einer Temperatur von 900 bis 1050°C. Dieser Phase schließt sich eine zweite Phase 2 an, in der eine schnelle Unterkühlung des Gefüges er reicht wird. Dies kann dadurch erfolgen, daß, wie es die durchgezogene Linie darstellt, ein Abschrecken auf Raumtemperatur erfolgt oder durch, wie gestrichelt dargestellt ist, eine Unterkühlung im Ofen mit anschließender quasi isothermer Umwandlung bei Temperaturen unter AR1. In einer dritten Phase 3 wird der Werkstoff auf Austenitisie rungstemperatur zwischen 770 und 830°C erwärmt, wobei sich Stickstoff- und Kohlenstoffatome in Form von feinstdispersen Karbiden fein ver teilt ausscheiden. Zur Vermeidung von Karbidvergrößerungen ist die Haltezeit auf der Austenitisierungstemperatur nur kurz.The single figure shows schematically the method according to the invention thermochemical-thermal treatment of case hardening steel. In the first phase called carbonitriding or case hardening a temperature of 900 to 1050 ° C. This phase includes one second phase 2, in which he rapid hypothermia of the structure is enough. This can be done by how the solid Line represents, quenching to room temperature or by subcooling in the oven, as shown in dashed lines subsequent quasi isothermal conversion at temperatures below AR1. In a third phase 3 the material is on austenitis temperature between 770 and 830 ° C, with nitrogen and carbon atoms in the form of finely divided carbides splits out. To avoid carbide enlargement, the Holding time at the austenitizing temperature only short.
In einer vierten Phase 4 erfolgt die Abkühlung auf Raumtemperatur oder wahlweise, wie gestrichelt dargestellt, eine Unterkühlung bis -120°C. Anschließend wird der Werkstoff in Phase 5 bei einer Temperatur von 160 bis 180°C und einer Haltezeit von zwei Stunden angelassen.In a fourth phase 4, cooling to room temperature or optionally, as shown in dashed lines, subcooling to -120 ° C. The material is then in phase 5 at a temperature of Annealed at 160 to 180 ° C and a holding time of two hours.
BezugszeichenlisteReference list
1 Korbinitrieren oder Einsatzhärten
2 Abkühlung
3 Austenitisieren
4 Abkühlung
5 Anlassen 1 basket nitriding or case hardening
2 cooling
3 Austenitizing
4 cooling
5 start
Claims (3)
Priority Applications (1)
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DE19924204982 DE4204982A1 (en) | 1992-02-19 | 1992-02-19 | Thermochemical-thermal treatment of case hardening steels - with deep cooling between hardening and tempering |
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DE19924204982 DE4204982A1 (en) | 1992-02-19 | 1992-02-19 | Thermochemical-thermal treatment of case hardening steels - with deep cooling between hardening and tempering |
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DE4204982A1 true DE4204982A1 (en) | 1993-08-26 |
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DE19924204982 Withdrawn DE4204982A1 (en) | 1992-02-19 | 1992-02-19 | Thermochemical-thermal treatment of case hardening steels - with deep cooling between hardening and tempering |
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Cited By (21)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0723034A3 (en) * | 1995-01-20 | 1996-12-11 | Dowa Mining Co | A gas carburising process and an apparatus therefor |
FR2813892A1 (en) * | 2000-09-13 | 2002-03-15 | Peugeot Citroen Automobiles Sa | Heat treatment of hypo-eutectoid tool steels incorporating a re-austenitising stage between stages of cementation, soaking and tempering |
FR2841907A1 (en) * | 2002-07-03 | 2004-01-09 | Ntn Toyo Bearing Co Ltd | Heat treatment process for bearing component involves carbonitriding at specified temperature, cooling, re-heating and hardening at lower temperature |
EP1510589A1 (en) * | 2003-08-29 | 2005-03-02 | NTN Corporation | Bearing's component, heat treatment method thereof, heat treatment apparatus, and rolling bearing |
EP1455102A3 (en) * | 2003-02-28 | 2006-01-18 | NTN Corporation | Transmission component, method of manufacturing the same, and tapered roller bearing |
US7334943B2 (en) | 2003-02-28 | 2008-02-26 | Ntn Corporation | Differential support structure, differential's component, method of manufacturing differential support structure, and method of manufacturing differential's component |
US7438477B2 (en) | 2001-11-29 | 2008-10-21 | Ntn Corporation | Bearing part, heat treatment method thereof, and rolling bearing |
US7490583B2 (en) | 2002-10-17 | 2009-02-17 | Ntn Corporation | Full-type rolling bearing and roller cam follower for engine |
US7594762B2 (en) | 2004-01-09 | 2009-09-29 | Ntn Corporation | Thrust needle roller bearing, support structure receiving thrust load of compressor for car air-conditioner, support structure receiving thrust load of automatic transmission, support structure for continuously variable transmission, and support structure receivin |
US7641742B2 (en) | 2004-01-15 | 2010-01-05 | Ntn Corporation | Rolling bearing and heat treatment method for steel |
US7744283B2 (en) | 2003-03-14 | 2010-06-29 | Ntn Corporation | Bearing for alternator and bearing for pulley |
US8066826B2 (en) | 2005-08-10 | 2011-11-29 | Ntn Corporation | Rolling-contact shaft with joint claw |
WO2012141639A1 (en) | 2011-04-13 | 2012-10-18 | Aktiebolaget Skf | Method of carbonitriding a steel component, the steel component and the use of the component |
DE102014113846A1 (en) * | 2014-09-24 | 2016-03-24 | Härterei Technotherm Gmbh & Co. Kg | Process for treating a ferrous material and treated ferrous material |
WO2016169560A1 (en) * | 2015-04-20 | 2016-10-27 | Schaeffler Technologies AG & Co. KG | Method for the mechanical-thermal treatment of reduced-carbon steels |
CN106399653A (en) * | 2016-09-27 | 2017-02-15 | 中国科学院理化技术研究所 | Method for improving impact toughness of 1Ni9 low-temperature steel |
RU2655875C1 (en) * | 2017-06-07 | 2018-05-29 | Акционерное общество "Федеральный научно-производственный центр "Нижегородский научно-исследовательский институт радиотехники" | Method of tempering thin-wall long components made of 12x2nvfa steel in controlled air flow |
DE102017117290A1 (en) * | 2017-07-31 | 2019-01-31 | Schaeffler Technologies AG & Co. KG | Process for producing a rolling bearing component |
CN111270051A (en) * | 2020-04-09 | 2020-06-12 | 重庆优特模具有限公司 | Heat treatment composite process and die steel thereof |
CN113174466A (en) * | 2021-04-30 | 2021-07-27 | 洛阳Lyc轴承有限公司 | Induction quenching method for 40Cr15Mo2VN high-nitrogen stainless bearing steel |
CN114150122A (en) * | 2021-12-06 | 2022-03-08 | 厦门擎华智能传动有限公司 | Processing method for improving gear ring for automobile drive axle |
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-
1992
- 1992-02-19 DE DE19924204982 patent/DE4204982A1/en not_active Withdrawn
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US2260249A (en) * | 1939-08-31 | 1941-10-21 | Battelle Memorial Institute | Case carburizing |
SU65612A1 (en) * | 1945-03-26 | 1945-11-30 | Б.А. Красюк | Method for increasing hardness of steel and cast iron products hardened and cooled to room temperature |
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SU1357441A1 (en) * | 1986-03-17 | 1987-12-07 | Краматорский Индустриальный Институт | Method of thermal treatment of cast cemented steel |
Cited By (31)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
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