EP0925377B1 - Verschleissbeständige nockenwelle und verfahren zu ihrer herstellung - Google Patents

Verschleissbeständige nockenwelle und verfahren zu ihrer herstellung Download PDF

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Publication number
EP0925377B1
EP0925377B1 EP97943775A EP97943775A EP0925377B1 EP 0925377 B1 EP0925377 B1 EP 0925377B1 EP 97943775 A EP97943775 A EP 97943775A EP 97943775 A EP97943775 A EP 97943775A EP 0925377 B1 EP0925377 B1 EP 0925377B1
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EP
European Patent Office
Prior art keywords
temperature
energy source
camshaft
layer
cementite
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
Application number
EP97943775A
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German (de)
English (en)
French (fr)
Other versions
EP0925377A1 (de
Inventor
Berndt Brenner
Andreas Wetzig
Dietmar Naunapper
Carsten Duschek
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Fraunhofer-Gesellschaft zur Förderung der Angewandten Forschung eV
Original Assignee
Fraunhofer-Gesellschaft zur Förderung der Angewandten Forschung eV
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Classifications

    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L1/00—Valve-gear or valve arrangements, e.g. lift-valve gear
    • F01L1/02—Valve drive
    • F01L1/04—Valve drive by means of cams, camshafts, cam discs, eccentrics or the like
    • F01L1/047—Camshafts
    • 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
    • C21D5/00—Heat treatments of cast-iron
    • 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
    • C21D9/30—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for crankshafts; for camshafts
    • 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
    • C21D1/06—Surface hardening
    • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/007—Ledeburite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S148/00—Metal treatment
    • Y10S148/902—Metal treatment having portions of differing metallurgical properties or characteristics

Definitions

  • the invention relates to the manufacture of highly wear-resistant ledeburitic surface layers of camshafts.
  • Ledeburitic surface layers have very good wear resistance sliding wear under hydrodynamic or mixed friction conditions.
  • the cams produced in this way have a coarse solidification structure, which is relatively coarse ledeburitic cementite and pearlite in the metallic matrix.
  • there are event zones that are characterized by unfavorable properties Damage to the remelting structure due to renewed exposure to temperature are characterized by the slow oscillation of the TIG torch.
  • a disadvantage of cams produced in this way is that the wear resistance is too low.
  • the cause of the low wear resistance lies in the rough Structure and the additional coarsening of the structure within the tempering zone.
  • the main shortcoming of the process is that the rate of solidification is too low.
  • the reason for this is the power density that is too low makes it necessary to work at relatively low feed speeds.
  • the remelted cam areas consist of a 0.3 mm to approximately on average 0.8 mm deep remelting zone.
  • the remelting zone contains ledeburitic cementite and pearlite in the metallic matrix.
  • ledeburitic cementite and pearlite in the metallic matrix.
  • the zone directly below the melting zone forms when the austenitizing temperature is exceeded due to the slow Cooling a newly pearlized zone slightly higher hardness than that of the Initial state. The drop in hardness therefore occurs directly at the edge of the melting zone one and is relatively rugged.
  • cams produced in this way are not the ones for one such a finely dispersed structure of ledeburitic cementite actually achieve possible wear resistance.
  • the reason for this is that the Perlite in the metallic matrix has a lower wear resistance than that Has cementite and therefore represents the weak point of the structure.
  • an optimal surface layer structure for wear stress requires one Layer structure, consisting of a thin layer near the surface, which the with the tribological load of adhesive loads, plastic Record deformations and cyclic elastic-plastic micro-expansions is capable, and an underlying support layer, which the stresses as a result which absorbs Hertzian pressure.
  • This support layer is only by a remelting layer can be formed. The greater remelting depth required for this leads to the lower feed rate necessary for this to be economical Disadvantages.
  • a cam with a surface layer structure that is better adapted to wear became known with PS EP 0 161 624.
  • the cam edge layer contains a cementite layer with a large proportion of cementite and below a martensitic layer, the remelting layer having a depth of 0.3 to 1.5 mm and the underlying hardening zone a thickness of 0.3 to 2.0 mm having.
  • Preheating can be dispensed with without consequences for crack formation, because with a very low power of 1360 - 2600 W at very low Rotation speeds of 0.7 to 1.0 U / min is worked. This corresponds about feed speeds of 80 to 130 mm / min. At these minor The introduced heat runs at feed speeds in front of the remelting spot and penetrates very far into the cam during the remelting. This reduces the quenching speed to such an extent that the Cracking stress is no longer reached during cooling. Through the however, the rate of solidification also becomes low reduced, which leads to a coarser formation of the ledeburitic cementite in the Comparison to laser or electron beam remelted cams.
  • Cams treated in this way exhibit despite the slow cooling rate compared to the cams remelted with TIG preheating Wear resistance. That can only be because that is in the metallic matrix formed perlite because of its higher formation Cooling speed is significantly more fine-grained. The potential of the possible However, property improvement through finely dispersed cementite formation can not be used.
  • cams produced in this way is therefore that they do not have optimal wear layers.
  • the reason for this is the relative rough formation of the solidification structure due to the low solidification speed and the formation of event zones.
  • the lack of the method is that due to the low power density and the slow feed rate one for a finely dispersed Microstructure formation too slow solidification rate occurs.
  • Another The deficiency is that the structure is macroscopically inhomogeneous and periodic has even coarser structures. The reason for this is renewed local temperature exposure to areas that have already cooled down to well above the austenitizing temperature due to the very slow oscillation movement of the TIG torch.
  • the aim of the invention is to provide a camshaft that is better protected against sliding wear and to propose a process for their manufacture.
  • the invention is based on the object, a microstructure and one Surface layer structure for camshafts and similarly loaded cast iron components specify the conditions of use of a sliding wear load with high Load stresses under hydrodynamic or mixed friction conditions to do better justice. Furthermore, a method is to be specified that for Setting finely dispersed structure works with high power densities, even without one thorough preheating avoids the formation of cracks and at the same time by a relatively high cooling rate between 600 ° C and 350 ° C the formation rough Pearlite largely suppressed.
  • this object is achieved with a wear-resistant camshaft made of cast iron, the edge layer of which consists of a ledeburitic remelting layer high cementite content and an underlying martensitic hardening zone consists, as shown in claims 1 and 2, solved.
  • the remelting layer consists of finely dispersed ledeburitic cementite with Wall thicknesses ⁇ 1 ⁇ m and a metallic matrix from a phase mixture of Martensite and / or bainite, residual austenite and less than 20% fine-grained pearlite with a lamella spacing ⁇ 0.1 ⁇ m.
  • the hardening layer underneath consists of a phase mixture of martensite and / or bainite, dissolved pearlite and Residual austenite.
  • the depths t s of the remelting layer specified in claim 2 are somewhat smaller according to the invention than known according to the prior art and thus use the supporting effect of the layer below in an economically advantageous manner.
  • the object is further achieved by a method for producing the wear-resistant camshaft with the help of a high-energy Remelting process as specified in claims 3 to 16, solved.
  • Short-term temperature cycles T1 and T2 succeed the previously existing ones Contradiction to demand a high rate of solidification and quenching as well as a relatively high and adjustable cooling rate between 600 ° C and 350 ° C on the one hand and the requirement for a low Cooling rate below about 300 ° C to solve.
  • this makes a finely dispersed solidification structure and a finely dispersed one Process of fixed conversions with an adjustable and relatively strong Coarse pearlite formation can be suppressed.
  • it is Cooling speed in the crack-critical temperature range is sufficiently low to To avoid cracks.
  • tempering zones avoided due to excessive temperature fluctuations during remelting can be.
  • the expedient embodiment of the invention described in claim 5 makes use of the fact that the rapid beam oscillation Dimensions of the energy beam in the feed direction and perpendicular to it relative can be set flexibly and independently of each other and that the specified oscillation frequencies the temperature oscillations are small enough to avoid event zones. This means that even with wide cams, small ones Melt pool lifespan can be achieved.
  • Claims 14 and 15 make advantageous use of the fact that about relatively small changes in the chemical composition of the Cast iron, the structure essential for the sliding wear properties can be changed significantly.
  • a cast iron camshaft with a chemical composition of 2.5 ... 3.2% C; 1.6 ... 2.5% Si; 0.3 ... 1.0% Mn; ⁇ 0.2% P; ⁇ 0.12% S; ⁇ 0.6% Cu; ⁇ 0.15% Ti; ⁇ 0.2% Ni; ⁇ 0.3% Cr; ⁇ 0.3% Mo; S c ⁇ 0.9 should be provided with an optimally wear-resistant and economically producible surface layer.
  • the cam diameter is 36 mm and the cam width is 14 mm.
  • the hardness of the initial structure is 250 HV 0.05.
  • the graphite formation is lamellar, the matrix almost completely pearlitic.
  • the realized temperature-time profile is shown schematically in FIG.
  • the process of generating the temperature-time cycle T1 becomes an inductive one Energy input selected.
  • the generator is an MF generator and has one Frequency of 10 kHz.
  • the inductor is a single-winding ring inductor with one 8 mm x 8 mm winding thickness and a coupling distance of 2.0 mm.
  • a 5.0 kW CO 2 laser serves as the energy source for generating the temperature-time cycle T2.
  • the laser beam is focused with an off-axis parabolic mirror with a focal length of 400 mm.
  • the cam surface is 30 mm out of focus.
  • the camshaft After the camshaft has been clamped in, it is rotated at a speed of 300 rpm.
  • the induction generator is set to an output of 70 kW.
  • the power density is p 1 ; 4000 W / cm 2 .
  • the laser is switched on as energy source S 2 .
  • the laser beam has the dimensions 16 mm x 2.5 mm, which leads to an average power density at the beam exit of approximately 1.15 • 10 4 W / cm 2 .
  • a CNC-programmed rotary movement of the cam is started with a relative feed speed of the laser beam of 600 mm / min as well as the corresponding compensating movements of the z-axis to keep the focus distance constant and the y-axis to ensure the vertical beam incidence.
  • the cam After switching off the laser, the cam cools in air. Because that Temperature field of inductive preheating at the beginning of laser beam melting only reached about 3 mm into the cam, the self-deterrence is sufficient to one to suppress continuous or coarse pearlite formation.
  • the result of the treatment is a 0.4 mm thick ledeburitic layer with a average hardness of 780 HV0.05. It consists of finely dispersed cementite with a Wall thickness of about 1 ⁇ m, residual austenite, martensite and bainite. The pearlite content is less than 20%. Below this is a martensitic support layer of 0.65 mm Thickness. In it, the hardness drops continuously from 780 HV0.05 to 400 HV0.05. she consists mainly of martensite, residual austenite, bainite and dissolved pearlite. The Edge layers are free of cracks.
  • the contents of martensite, austenite, bainite and pearlite can be changed by varying the preheating time t 1 of the temperature-time cycle T 1 towards larger times and the peak temperature T 1max towards higher temperatures.
  • a higher pearlite content can also be set for wear stresses at higher temperatures without violating the inventive concept.
  • the formation of the cementite can also be made more finely dispersed.
  • Laser or electron beam remelting after conventional preheating (dash-dotted line), on the other hand, has very high heating speeds, short melt bath life and high solidification and quenching speeds, which lead to finer cementite formation. Because of the high conventional preheating temperature T v , however, the cooling rate in the temperature range Mp is so low that relatively coarse pearlite is formed.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Heat Treatment Of Articles (AREA)
EP97943775A 1996-09-13 1997-09-12 Verschleissbeständige nockenwelle und verfahren zu ihrer herstellung Expired - Lifetime EP0925377B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE19637464 1996-09-13
DE19637464A DE19637464C1 (de) 1996-09-13 1996-09-13 Verschleißbeständige Nockenwelle und Verfahren zu ihrer Herstellung
PCT/DE1997/002072 WO1998011262A1 (de) 1996-09-13 1997-09-12 Verschleissbeständige nockenwelle und verfahren zu ihrer herstellung

Publications (2)

Publication Number Publication Date
EP0925377A1 EP0925377A1 (de) 1999-06-30
EP0925377B1 true EP0925377B1 (de) 2001-12-12

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Application Number Title Priority Date Filing Date
EP97943775A Expired - Lifetime EP0925377B1 (de) 1996-09-13 1997-09-12 Verschleissbeständige nockenwelle und verfahren zu ihrer herstellung

Country Status (6)

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US (1) US6398881B1 (cs)
EP (1) EP0925377B1 (cs)
JP (1) JP2001503104A (cs)
CZ (1) CZ295308B6 (cs)
DE (2) DE19637464C1 (cs)
WO (1) WO1998011262A1 (cs)

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10137776C1 (de) * 2001-08-02 2003-04-17 Fraunhofer Ges Forschung Verfahren zur Erzeugung von verschleissbeständigen Randschichten
WO2006123497A1 (ja) * 2005-05-18 2006-11-23 Hitachi Construction Machinery Co., Ltd. 摺動部材
DE102005054709A1 (de) * 2005-11-17 2007-05-31 Federal-Mogul Burscheid Gmbh Verfahren zur Herstellung von Gleit-und/oder Gegenringen einer Gleitringdichtung
US20070116889A1 (en) * 2005-11-18 2007-05-24 Federal Mogul World Wide, Inc. Laser treatment of metal
DE102005061980B4 (de) * 2005-12-23 2010-02-18 Audi Ag Verfahren zur Herstellung einer Nockenwelle und Nockenwelle
US20070254111A1 (en) * 2006-04-26 2007-11-01 Lineton Warran B Method for forming a tribologically enhanced surface using laser treating
US20090078343A1 (en) * 2007-09-24 2009-03-26 Atlas Copco Secoroc Llc Earthboring tool and method of casehardening
DE102013008396B4 (de) 2013-05-17 2015-04-02 G. Rau Gmbh & Co. Kg Verfahren und Vorrichtung zum Umschmelzen und/oder Umschmelzlegieren metallischer Werkstoffe, insbesondere von Nitinol
GB201600645D0 (en) * 2016-01-13 2016-02-24 Rolls Royce Plc Improvements in additive layer manufacturing methods
DE102019003511A1 (de) * 2019-05-17 2020-11-19 VoItabox AG Verfahren zum thermischen und insbesondere stoffschlüssigen Verbinden, vorzugsweise Verschweißen, von Aluminiumgehäuseteilen
US20220314372A1 (en) * 2021-03-30 2022-10-06 GM Global Technology Operations LLC System and method for making an enhanced cast iron workpiece having increased lubricant retention
DE112023002692T5 (de) * 2022-06-20 2025-04-10 Cummins Inc. Systeme und verfahren zur verbesserung der ermüdungsfestigkeit von nockenwellen auf eisenbasis

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DE4237484A1 (de) 1992-11-06 1994-05-11 Mauser Werke Oberndorf Verfahren und Vorrichtung zum Umschmelzen einer Werkstückoberfläche eines Werkstückes, insbesondere einer Nocken- oder Kurbelwelle
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DE59403740D1 (de) * 1993-05-19 1997-09-18 Fraunhofer Ges Forschung Verfahren zur materialbearbeitung mit diodenstrahlung

Also Published As

Publication number Publication date
CZ83899A3 (cs) 2000-05-17
US6398881B1 (en) 2002-06-04
DE59705796D1 (de) 2002-01-24
CZ295308B6 (cs) 2005-07-13
WO1998011262A1 (de) 1998-03-19
EP0925377A1 (de) 1999-06-30
JP2001503104A (ja) 2001-03-06
DE19637464C1 (de) 1997-10-09

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