WO2010000222A1 - Pièce en acier à surface particulièrement résistante et son procédé de production - Google Patents

Pièce en acier à surface particulièrement résistante et son procédé de production Download PDF

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Publication number
WO2010000222A1
WO2010000222A1 PCT/DE2009/000845 DE2009000845W WO2010000222A1 WO 2010000222 A1 WO2010000222 A1 WO 2010000222A1 DE 2009000845 W DE2009000845 W DE 2009000845W WO 2010000222 A1 WO2010000222 A1 WO 2010000222A1
Authority
WO
WIPO (PCT)
Prior art keywords
component
temperature
quenching
carbonitriding
low temperature
Prior art date
Application number
PCT/DE2009/000845
Other languages
German (de)
English (en)
Inventor
Oswald Bayer
Horst Masuch
Wolfgang May
Werner Trojahn
Original Assignee
Schaeffler Kg
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Schaeffler Kg filed Critical Schaeffler Kg
Publication of WO2010000222A1 publication Critical patent/WO2010000222A1/fr

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Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • 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
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
    • 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
    • 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
    • C23C8/80—After-treatment

Definitions

  • the invention is in the field of mechanical engineering and more specifically in the field of tribology, that is, the design of components with the aim of increasing the stability, resistance and durability of components against surface wear and to optimize friction parameters.
  • the invention is concerned with steel components which are subject to increased surface loading, for example when used in rolling bearings.
  • such components can be made from highly resistant steel grades or similar alloys in order to achieve both coefficient of friction as well as to optimize hardness and abrasion.
  • this is often not possible because of the cost of materials or, for example, because the components can not or should not be made homogeneous for various reasons.
  • the present invention has for its object to provide a steel component and a method for its production, which combine a high material hardness with a low tendency to cracking and high wear resistance to abrasion with the lowest possible production costs in the area of a particularly loaded surface.
  • a shell component is carbonitrided, that is, exposed to carbon and nitrogen at elevated temperatures so that corresponding atoms can diffuse in the surface region.
  • the shell component can be stored even further at a corresponding temperature, for example between 820 ° C and 880 ° C (hardening temperature), in order to achieve a substantial conversion of ferrite to austenite (austenitization).
  • quenching ie rapid cooling, for example to room temperature (20 ° C.), at least at a cooling rate which corresponds to the so-called first critical cooling rate, which is decisive for martensitic hardening.
  • At least a portion of the austenite is converted to martensite, which has a desired high hardness at least in the surface region.
  • the component is then stored for a time at a low temperature that is at least below 0 ° C to reduce retained austenite.
  • the shell part has a carbon content of between 0.8% and 1.1% in parts by weight, a high hardness can be achieved with the appropriately formed martensitic part if a corresponding deep cooling takes place. Due to the preceding carbonitriding, the carbon content is particularly high in the surface area, so that the achievable by the storage at low temperature outside hardness particularly high values (62 to 67 HRC), while below the surface layer has a hardness of at least 60 HRC and a Austenithaltsgehalt less than 10% is present.
  • the conversion of retained austenite into martensite is not as pronounced as in the core area because of the increased carbon content and must be supported by cold storage.
  • the sulfur content to less than 0.01 percent by weight results in the surface area a good toughness against stress-induced cracking.
  • the process according to the invention can advantageously be configured by storing the greenware component at a hardening temperature between 820 ° C. and 880 ° C. for at least 20 minutes between carbonitriding and quenching.
  • the storage time is advantageously at least 20 minutes after the heating, wherein in this hardening process a substantial austenitization takes place. This increases the rate of martensite achievable by deterrence.
  • the shell component is stored at a temperature between 600 ° C. and 750 ° C. for at least one hour.
  • the shell component is exposed to an annealing treatment at a temperature between 500 ° C and 750 ° C.
  • An advantageous embodiment of the invention provides that the shell component between the carbonitriding and the subsequent treatment step is cooled to room temperature.
  • the actual reduction of the residual austenite content takes place by further cooling and storage of the component at a low temperature which is advantageously below 0 ° C., particularly advantageously below -40 ° C., in particular -100 ° C. and occasionally advantageously even below -150 ° C is.
  • the component can also be brought to its temperature by means of liquid nitrogen and stored there in order to achieve the greatest possible conversion of the retained austenite into martensite.
  • This storage can last for example at least one hour.
  • the component After storage at low temperature, the component can be heated and tempered.
  • the tempering at different temperature levels is conceivable, wherein advantageously the first tempering stage is provided between 120 ° C and 200 ° C.
  • the martensite passes into a modification step called cubic martensite.
  • the invention relates, in addition to a method for producing a steel component, also to a steel component which has been described Method is prepared and having a Restaustenitgehalt in the range of the surface between 15% and 40%.
  • the steel component In the core area, the steel component has a much lower austenite content than in the surface area, for example less than 10%. As a result, the surface area becomes extremely wear-resistant as a result of a tough residual austenite content, high residual compressive stresses and high hardness, the component also having an outstanding resistance to stress-induced cracking and toughness due to the low sulfur content.
  • FIG. 1 shows the spindle of a machine tool
  • FIG. 2 shows a spindle bearing in the form of an angular ball bearing
  • FIG. 3 shows a schematic process representation of the method according to the invention.
  • the inventive method is particularly suitable for the production of elements for rolling bearings, in particular rolling bearings for high-speed spindles of machine tools or other fast-rotating and highly loaded components.
  • elements for rolling bearings particularly high demands are placed on the wear resistance of the steel in the rolling bearing.
  • ceramic rolling elements ceramic rolling elements (cylindrical rollers or balls) are used.
  • lubrication with grease or oil takes place.
  • 1 shows a spindle 1 of a machine tool not shown in detail, which is rotatably mounted in a plurality of bearings and by means of a drive 2 is driven to rotate.
  • two angular contact ball bearings 3, 4 which prevent axial movement of the spindle in the direction of the arrow 5 and support the spindle in the arrow 5 opposite axial direction.
  • two angular contact ball bearings 6, 7 are shown, which prevent axial movement of the spindle 1 in the direction of the arrow 8 and thus support the spindle in the direction opposite to the arrow 8 axial direction.
  • the respective angular contact ball bearings 3, 4, 6, 7 provide for a radial support and storage.
  • the corresponding rolling elements (balls) are designed as ceramic body.
  • Each of the inner and / or outer ring 9, 10 of a bearing is at least in the region of its tread, which comes into contact with the rolling elements, executed particularly wear-resistant.
  • FIG. 2 shows enlarged an individual angular contact ball bearing with an outer ring 12, which has a tread 13, and an inner ring 14, which has a running surface 15 for a spherical rolling element 16.
  • the running surfaces 13, 15 are arranged asymmetrically such that an axial relative movement in the direction of the arrows 17, 18 of the two bearing rings is prevented from one another and the bearing is supported accordingly.
  • a bearing cage 19 and a multi-part bearing plate 20, 21 are shown schematically in the figure.
  • the bearing is typically oil lubricated and is suitable for high speeds and exceptionally long tool life.
  • FIG. 3 schematically shows a diagram of the inventive method on the basis of time duration and temperature data for different method steps.
  • the process starts at a temperature Temp 5, which can be between 820 ° C and 930 ° C.
  • the crude steel component which is homogeneous at the beginning of the process and between 0.8 and 1, 1 weight percent carbon, 1, 3 to 2 weight percent chromium, 0.2 to 1, 5 weight percent manganese, 0.2 to 0.9 weight percent Silicon and containing less than 0.01 percent by weight of sulfur and other common and unavoidable impurities and accompanying elements is subjected to carbonitriding in an ammonia-enriched hydrocarbon gas at this temperature, wherein the carbon content in the region of the tread (overrun functional area) to 0 , 9% to 1, 4% and the nitrogen content is enriched to 0.05% to 0.5%.
  • the increase of the stated carbon and nitrogen contents extends to a depth between 1% and 6% of the corresponding component diameter in the area of the overrun surface.
  • the carbonitriding at the temperature Temp 5 take place over two to twelve hours and its end is characterized by the time t 1 in the diagram. Thereafter, the temperature can be lowered to room temperature Temp 2, held there from t2 to t3 and then held back to a temperature Temp 4 between 820 ° C and 880 ° C until time t 4.
  • this hardening between t 3 and t 4 at a temperature between 820 ° C and 880 ° C there can also be a heat treatment between 500 ° C and 750 ° C or an annealing between 500 ° C and 750 ° C.
  • the transition between the carbonitriding temperature Temp 5 and the hardening temperature Temp 4 can also take place directly without intermediate cooling to room temperature, as indicated by the dotted line 22.
  • a quench is provided at a cooling rate which exceeds the first critical cooling rate for a martensitic transformation and is typically up to room temperature Temp 2. However, it may also be cooled down to another lower temperature, which may be lower when the room temperature can be Temp 2.
  • the component can be further cooled down to time t 5 up to a temperature of temp. 1 which is well below room temperature, often advantageously below -40 ° C. or -100 ° C., for example also at the temperature of the liquid nitrogen can.
  • a temperature of temp. 1 which is well below room temperature, often advantageously below -40 ° C. or -100 ° C., for example also at the temperature of the liquid nitrogen can.
  • the component is stored until time t 6 over a period of time which provides complete cooling and then a storage time of at least half an hour.
  • Toughening to increase toughness typically occurs at the first tempering temperature Temp 3 in the range between 120 ° C and 200 ° C.
  • the treatment described creates a steel component with exceptional wear resistance and resistance to stress cracks in the surface area and a high hardness between 62 and 67 HRC in the surface area. Limiting the sulfur content prevents the excretion of larger sulphides which would otherwise destroy the fracture toughness achieved by the treatment.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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)
  • Rolling Contact Bearings (AREA)

Abstract

L'invention concerne une pièce en acier (12, 14) particulièrement résistante à l'usure, obtenue par un procédé consistant à prendre une d'abord pièce brute présentant une teneur en soufre inférieure à 0,01 pour-cent en poids, et une teneur en carbone comprise entre 0,8% et 1,1%, et à la soumettre à un traitement thermique comprenant une carbonitruration, un durcissement, une trempe et un entreposage à basse température. Ce procédé confère à la pièce une surface particulièrement dure et résistante à la fissuration.
PCT/DE2009/000845 2008-07-01 2009-06-19 Pièce en acier à surface particulièrement résistante et son procédé de production WO2010000222A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102008031107.3 2008-07-01
DE102008031107.3A DE102008031107B4 (de) 2008-07-01 2008-07-01 Stahlbauteil mit beanspruchbarer Oberfläche und Verfahren zu seiner Herstellung

Publications (1)

Publication Number Publication Date
WO2010000222A1 true WO2010000222A1 (fr) 2010-01-07

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PCT/DE2009/000845 WO2010000222A1 (fr) 2008-07-01 2009-06-19 Pièce en acier à surface particulièrement résistante et son procédé de production

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DE (1) DE102008031107B4 (fr)
WO (1) WO2010000222A1 (fr)

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RO92459A2 (fr) * 1985-06-19 1987-09-30 Institutul De Cercetare Stiintifica Inginerie Tehnologica Si Proiectari Pentru Sectoare Calde,Ro Procede pour le traitement thermique des outils
US5427457A (en) * 1991-07-18 1995-06-27 Nsk Ltd. Rolling bearing
EP1143018A2 (fr) * 2000-03-28 2001-10-10 Nsk Ltd Palier à roulement
US20020066502A1 (en) * 2000-10-06 2002-06-06 Hiroshi Tako Bearing for main spindle of machine tool
DE10161721A1 (de) * 2001-12-15 2003-06-18 Kugelfischer G Schaefer & Co Wälzlagerkomponenten mit verschleißfester Oberfläche
JP2006322017A (ja) * 2005-05-17 2006-11-30 Nsk Ltd 転がり軸受
KR100793702B1 (ko) * 2007-03-30 2008-01-14 현대 파워텍 주식회사 자동변속기용 기어류 및 샤프트의 열처리 방법

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RO92459A2 (fr) * 1985-06-19 1987-09-30 Institutul De Cercetare Stiintifica Inginerie Tehnologica Si Proiectari Pentru Sectoare Calde,Ro Procede pour le traitement thermique des outils
US5427457A (en) * 1991-07-18 1995-06-27 Nsk Ltd. Rolling bearing
EP1143018A2 (fr) * 2000-03-28 2001-10-10 Nsk Ltd Palier à roulement
US20020066502A1 (en) * 2000-10-06 2002-06-06 Hiroshi Tako Bearing for main spindle of machine tool
DE10161721A1 (de) * 2001-12-15 2003-06-18 Kugelfischer G Schaefer & Co Wälzlagerkomponenten mit verschleißfester Oberfläche
JP2006322017A (ja) * 2005-05-17 2006-11-30 Nsk Ltd 転がり軸受
KR100793702B1 (ko) * 2007-03-30 2008-01-14 현대 파워텍 주식회사 자동변속기용 기어류 및 샤프트의 열처리 방법

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Publication number Publication date
DE102008031107A1 (de) 2010-01-07
DE102008031107B4 (de) 2016-09-15

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