EP2213790A1 - Corps de cylindre pour un cylindre destiné au traitement d'un matériau et procédé de fabrication d'un corps de cylindre - Google Patents

Corps de cylindre pour un cylindre destiné au traitement d'un matériau et procédé de fabrication d'un corps de cylindre Download PDF

Info

Publication number
EP2213790A1
EP2213790A1 EP10150614A EP10150614A EP2213790A1 EP 2213790 A1 EP2213790 A1 EP 2213790A1 EP 10150614 A EP10150614 A EP 10150614A EP 10150614 A EP10150614 A EP 10150614A EP 2213790 A1 EP2213790 A1 EP 2213790A1
Authority
EP
European Patent Office
Prior art keywords
graphite
roller body
roller
peripheral edge
edge zone
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.)
Granted
Application number
EP10150614A
Other languages
German (de)
English (en)
Other versions
EP2213790B1 (fr
Inventor
Ulrich Severing
Bernd Eppli
Lutz Krodel-Teuchert
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
SHW Casting Technologies GmbH
Original Assignee
SHW Casting Technologies GmbH
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 SHW Casting Technologies GmbH filed Critical SHW Casting Technologies GmbH
Publication of EP2213790A1 publication Critical patent/EP2213790A1/fr
Application granted granted Critical
Publication of EP2213790B1 publication Critical patent/EP2213790B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • D—TEXTILES; PAPER
    • D21—PAPER-MAKING; PRODUCTION OF CELLULOSE
    • D21F—PAPER-MAKING MACHINES; METHODS OF PRODUCING PAPER THEREON
    • D21F3/00—Press section of machines for making continuous webs of paper
    • D21F3/02—Wet presses
    • D21F3/08—Pressure rolls
    • 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
    • C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/04—Cast-iron alloys containing spheroidal graphite
    • D—TEXTILES; PAPER
    • D21—PAPER-MAKING; PRODUCTION OF CELLULOSE
    • D21G—CALENDERS; ACCESSORIES FOR PAPER-MAKING MACHINES
    • D21G1/00—Calenders; Smoothing apparatus
    • D21G1/02—Rolls; Their bearings
    • D21G1/0246—Hard rolls

Definitions

  • the invention relates to a roller body for a roller for the treatment of a material, preferably a thermal or mechanical treatment of a web material. Furthermore, the invention relates to a method for producing such a roll body.
  • the roller body may already be part of a roller having at the axial ends of the roller body pin flanges for their pivot bearing.
  • the invention also relates to the roll body as such, before it is assembled with other components to form a roll.
  • rolls of several meters in length and more than one meter in diameter are used to produce the finished paper web from cellulose sludge by means of thermal and mechanical treatment.
  • Rollers made of chilled cast iron, in particular shell-cast iron, or forged steel are used.
  • the cast iron bodies are produced by chill casting, usually standing in static chill casting.
  • the ring molds is achieved that sets in the outer peripheral edge zone, the shell, a carbide, white cast iron.
  • the peripheral edge zone or shell solidifies metastable, white, the carbon is bound there in the form of carbides.
  • the melt solidifies in gray the carbon is present as free graphite in the iron matrix.
  • the required hardness at the outer circumference of the roll body, the surface hardness, is ensured by the material of the shell, the white cast iron.
  • the hardness is set at the surface and in the near-surface depth range.
  • the disadvantage of shell casting is the impact brittleness, its sensitivity to sudden changes in temperature, and uneven wear on the outer circumference of the roll due to the carbides contained in the white iron.
  • the EP 0 505 343 A1 proposes to overcome the disadvantages mentioned that the roll body is cast from an iron-based alloy, so that a pearlitic or ferritic-pearlitic microstructure is formed which is at least 60% pearlitic.
  • the iron-based alloy contains 3.0 - 3.8% C, 1.5 - 3.0% Si and 0.5 - 0.9% Mn. Maximum levels are given for P and S.
  • As further alloying elements Cr, Ni, Cu, Mg, Mo, Sn or Al are used.
  • the roll body is surface hardened, called induction and flame hardening, and annealed after the martensitic transformation so that the roll body receives a temper martensite structure in its peripheral edge zone. With the martensitic structure of the peripheral edge zone is accompanied by a considerable risk of cracking.
  • roller bodies made of forged steel the mentioned material problems can be solved.
  • Surface hardness and hardening depth are adjusted on the roll body by subsequent thermal surface treatment.
  • the production takes place from a forging block, the weight of which depends on the size of the roll body.
  • Roll body as the invention relates to weigh many tons, large roll body, for example, have a weight of about 50 tons or more.
  • the weight of the forge block can be up to 200t.
  • a hollow forging is possible in this weight range only with great effort.
  • high demands are placed on the inner quality of the forged steel with regard to defects, inclusions and the like. The application is therefore very low.
  • the roll body should be able to replace the known roll body of shell hard casting, in particular the required hardness on the surface and in the near-surface depth range, but not in the application disadvantageous unevenness in wear and impact brittleness.
  • the risk of cracking associated with a martensite shell should also be avoided.
  • the invention is based on a roller body which is cast from a single iron-based alloy.
  • the iron-base alloy forms in the roll body a radially inner zone of the roll body of gray cast iron, preferably ductile iron, and the inner zone enclosing a the outer periphery of the roller body containing peripheral edge zone having a surface hardness greater than 400HV on the outer circumference, as is the case for the hitherto predominantly used for shell hard casting.
  • the roll body can be seen in cross-section of full material, so that the radially inner zone of gray cast iron forms a central core of the roll body.
  • the roll body may instead also be a hollow roll shell, so that the radially inner zone is an annular zone.
  • the inner zone and the peripheral edge zone are cast in one piece, the use of the two terms is intended to indicate the difference in the microstructure present in the two zones, hereinafter simply microstructure.
  • the peripheral edge zone consists either of fine-grained or very fine-grained perlite with vermicular graphite or preferably spheroidal graphite or of an intermediate-layer structure, preferably ADI with spherical or vermicular graphite.
  • the fine-grained pearlite is also known as sorbitol and the finest-grained as troostite.
  • the invention combines the advantages of the cast roll body with those of the roll body of forged steel and avoids the risk of cracking associated with a martensite shell. As a cast body, it can be made significantly cheaper over its entire axial length in a cast and thus compared to a roll body made of forged steel.
  • the gray cast iron inner zone is easy to machine, for example, by cutting.
  • near-surface pheripheral holes for the passage of a thermal fluid can be created in the inner zone.
  • the hardness profile of the circumferential edge zone that is to say the course of the hardness applied over the roller radius, corresponds at least to the hardness profile of conventional rollers and can be controlled by the heat treatment process.
  • the mechanical strength is significantly improved compared to shell casting, which is reflected in higher 0.2% yield strength, tensile strength and elongation at break values.
  • the elongation at break is advantageously increased, in particular the risk of cracking is significantly reduced.
  • the graphite spheres which form the spheroidal graphite in the solidified peripheral edge zone have a maximum size which corresponds to a guide number of at least 5 (0.06-0.12 mm) according to EN ISO 945 corresponds.
  • the excretion of graphite in the form of only such small graphite balls is also advantageous for the mechanical strength and is achieved in the casting process by adjusting the cooling rate of the melt.
  • the melt is cooled from the outside, from the outer circumference, wherein the cooling rate is on the one hand so small that sets in the peripheral edge zone to the outer periphery or virtually to the outer periphery of a ductile iron structure, but on the other hand is so large that the Graphite spheres of the peripheral edge zone are smaller than in the conventional nodular cast iron, for example, when poured into a sand mold.
  • the nodular graphite has almost only, preferably only, graphite balls having a maximum size which has a guideline value of at least 6 (0.03-0.06 mm), more preferably at least 7 (0.015 mm).
  • the graphite spheres of the spheroidal graphite vessel which is preferably also present in the inner zone, can be larger.
  • the proportion of spheroidal graphite on the free graphite of the solidified peripheral edge zone is at least 80%, preferably at least 90%, and from the graphite spheres of the spheroidal graphite graphite of the peripheral edge zone correspond to at least 90%, preferably at least 95%, the above requirements for the size of Graphitkugeln. This standard is the currently valid EN ISO 945: 1994.
  • the vermicular graphite particles if present, have a maximum size, in this case the length, of 0.12 mm, more preferably at most 0.06 mm, and even more preferably at most 0.03 mm. Of the total vermicular graphite particles present, at least 90%, preferably at least 95%, fall into this size range.
  • the carbide content makes up at most 3%.
  • Shares in% are always understood as% by mass, ie as% of the total mass. With respect to any carbide content, this means that it is less than 5 mass% of the mass of the peripheral edge zone as a whole, including the carbide portion, preferably at most 3 mass%.
  • a white cast iron typically has a carbide content of 15% or more. Also due to the significantly reduced carbide content and the microcrape effect thus reduced, the material of the circumferential edge zone of the roll body according to the invention has significantly improved strength values compared to white cast iron.
  • the roll body with the structure according to the invention - radially inner zone in gray cast iron, preferably in spheroidal graphite, and peripheral edge zone in fine or feinststreifigem perlite or as Eisencarengemosge, each with vermicular or preferably nodular graphite - may be part of a roll for the material treatment, either a roller yet outside a machine or a roller already installed in a machine, for example a paper machine.
  • the roller accordingly has the roller body and at the two axial ends of the roller body in each case a journal flange for their pivot bearing, optionally the introduction of a torque or the supply or discharge of a thermal fluid.
  • journal flanges of a roller this means, for example, that the journal flanges can serve either only the rotary bearing or the rotary bearing and additionally only the introduction of the torque or in a further alternative of the rotary bearing and the supply or discharge of a thermal fluid.
  • one of the spigot flanges can fulfill all four functions in combination, ie serve the pivot bearing and initiation of a torque, as well as the supply and discharge of a thermal fluid.
  • the invention also relates to a roller body as such, which is provided only for assembly with further components of such a roller, for example the said journal flanges.
  • the roll body according to the invention is at least finished insofar as it is no longer subjected to any thermal treatment which specifically serves to adjust the microstructure. Any after-treatment, for example grinding or polishing, optionally machining or, for example, also mechanical training and, in principle, thermal treatments which in particular do not change the structure claimed for the peripheral edge zone to such an extent that it no longer corresponds to the claimed invention. but are excluded from this.
  • the roll or the roll body can be used in particular for the thermal or mechanical treatment of a web material, preferably in papermaking, for example as a smoothing or calendering roll.
  • the roller or the roller body can also be used as an embossing roll to engrave web material, for example a nonwoven web material.
  • Another preferred application is material shredding.
  • the roller or the roller body can be used for squeezing, for example, hops or other fruits, in the example as squeezing roller or squeeze roller.
  • a method for producing the roll body comprises at least the following steps: the roll body is cast from a melt of an iron-based alloy so that the melt is stable both in the radially inner zone of the roll body and in the radially adjoining peripheral edge zone reaching to the outer periphery Cast iron and solidified at least in the peripheral edge zone, but preferably also in the inner zone in a nodular cast iron structure or a cast structure with vermicular graphite.
  • the matrix of the cast iron is pearlitic / ferritic, with the proportion of pearlite being greater than 90% and that of the ferrite being less than 10%.
  • the proportion of the perlite of the cast iron matrix is greater than 95% and that of the ferrite is less than 5%.
  • any amount of carbide in the peripheral edge zone is less than 5%, preferably less than or equal to or less than 3%.
  • the roll body obtained with this cast structure is bonded to the outer periphery by means of a thermal surface treatment, i. hardened on the peripheral surface, and in the peripheral edge zone.
  • the thermal surface treatment is carried out so that the peripheral edge zone forming casting material, cast iron with nodular graphite or nodular graphite, with nodular graphite being preferred, is converted into fine or very fine-grained perlite with vermicular or nodular graphite or into an interstage structure with spheroidal graphite or vermicular graphite. More specifically, the cast iron matrix is converted into said perlite or interstage structure, and the free graphite already precipitated by the casting as a stable phase is retained. Further, the melt is not poured into sand, but against mold to control the cooling rate to be able to. Chill casting can be static or instead dynamic, ie centrifugal casting.
  • the roll body is expediently poured upright, ie with its longitudinal axis in vertical alignment.
  • the casting against mold allows a more precise adjustment of the cooling rate, in particular via the choice of the thickness of the mold measured radially to the longitudinal axis of the roll body, the specific or the absolute heat capacity, the thermal conductivity or the mass of the mold or a suitable combination of such adjustment parameters by the mold.
  • the cooling rate can be controlled, for example, by a single or, preferably, a combination of several of the following: lower die thickness, use of a die of a lower heat capacity material , Use of a mold of lower thermal conductivity, lower mold mass, in each case in comparison with a mold for casting a roll body of the same geometry and the same material in conventional hard shell casting.
  • the cooling rate is set by cooling the mold not only so small that the melt solidifies stable in the peripheral edge zone, but on the other hand so large that, as explained above for the preferred spheroidal graphite nodular graphite is precipitated in the peripheral edge zone in graphite spheres with a maximum size corresponding to the guideline number 5, preferably a maximum size of the guideline number 6, according to EN ISO 945.
  • the graphite balls are particularly preferably in the size range between 7 and 8 according to EN ISO 945, ie at the guideline number 7/8.
  • Such a fine graphite precipitation has a positive effect on the mechanical strength.
  • the fine precipitation of the graphite also increases the regularity of the surrounding cast iron matrix, which in turn is advantageous for the conversion of this basic structure present after casting into fine-grained or ultraprecipitated perlite or into an interstage structure.
  • Due to the thermal surface treatment of the roll body is hardened to a radial depth of advantageously at least 3mm, preferably at least 5mm by the cast iron matrix to at least in this Einhärttiefe in the fine or feinststreifigen perlite or the interstitial structure is converted.
  • a Einhärttiefe of 7mm is optimal.
  • a hardening depth of more than 10 mm should not be ruled out, large hardening depths produce material tensions when the temperature changes, with the risk that the hardened layer, the peripheral edge zone, will flake off.
  • Flame hardening and induction hardening are particularly suitable as methods of thermal surface treatment, preference being given to induction hardening, since flame hardening is limited to the lower part of the hardening depth, generally even below 3 mm. Flame hardening is therefore primarily for roll body with small diameters of up to 600 mm into consideration, although the induction hardening is also given preference here.
  • the peripheral edge zone is briefly heated to the austenitic region, preferably to at least 880 ° C. and particularly preferably to about 950 ° C.
  • the heated material is cooled by a surface cooling, preferably by means of a water quenching, in a short time to below 100 ° C, preferably below 50 ° C, so that the isothermal conversion takes place in the fine or feinststreifigen perlite.
  • a surface cooling preferably by means of a water quenching
  • a higher cooling rate is set, but still not so large that a significant martensitic transformation takes place. Martensite is ideally avoided because of the associated risk of cracking.
  • the cast iron of the peripheral edge zone therefore has, in preferred embodiments, a martensite start temperature M s which is below the values given above, ie below 100 ° C., preferably below 50 ° C.
  • the material of the peripheral edge zone has a martensite start temperature M s which is below room temperature, ie below 20 ° C.
  • the surface hardened roll body is advantageously tempered to relieve stresses.
  • the tempering temperature is above the temperature that reaches the roller body in later operation at the most, advantageously above 30 ° C, preferably a tempering temperature in the range of 300 to 350 ° C. Even after such an annealing, the roll body in the peripheral edge zone on the fine or feinststreifg pearlitic structure with spherical or vermicular graphite or the interstage structure with spherical or vermicular graphite.
  • the iron-base alloy has a carbon content of preferably at least 3%, preferably at most 4%.
  • the silicon content is preferably at least 1.7 and preferably at most 2.4%, whereby these are also always% by mass.
  • the degree of saturation Sc of the alloy is preferably in the range of 0.97 to 1.03, preferably it is slightly smaller than 1.0, so that the melt is slightly hypoeutectic.
  • a preferred alloying partner is copper, as a perlite former, and in a proportion of preferably at least 0.5 and preferably at most 1.3%.
  • a particularly preferred alloying partner is also nickel, which is alloyed in a proportion of preferably more than 0.3%, more preferably more than 0.5%, and preferably at most 1.5%. Nickel increases the toughness and makes the material corrosion-resistant.
  • nickel is of particular value for preventing martensite transformation during curing. If the iron base alloy contains both silicon and nickel, it is advantageous if the silicon content decreases with increasing nickel content and the nickel content decreases with increasing silicon content. Preference is given to a silicon content from the lower half of the range specified for silicon and a nickel content from the middle part of the range specified for nickel.
  • a particularly preferred iron alloy contains as alloying partners both Ni and Cu with preferably at least the minimum proportions indicated for each.
  • Optional alloying partners are also manganese and tin, manganese preferably in the range of 0.3 to 0.45%, tin preferably in the range of 0.005 to 0.015%. Compared to the other alloying elements mentioned above, however, the meaning of manganese and tin is reversed.
  • a preferred iron-based alloy contains C, Si, Ni and Cu within the preferred limits of the proportions, optionally Mn and Sn, as well as unavoidable residual P and S and the remainder Fe. Any proportions of phosphorus and sulfur are advantageously each well below 0.1%, more preferably still well below 0.05%.
  • FIG. 1 shows a roller for the treatment of a web material, for example a calender roll, with a roller body 1 and two flange pins 2 and 3, one of which is mounted on the left and the other on the right front side of the roller body 1.
  • the roller is rotatably mounted in the region of the journal flanges 2 and 3 about an axis of rotation R or provided for pivotal mounting.
  • a thermal fluid can be supplied, which can be derived via the other or preferably the same pin flange 2 or 3 again.
  • the roller body 1 passes through from one axial end to the other continuous, located near the outer periphery of the roller body 1, peripheral tempering 4, which are flowed through during the thermal treatment of the material from the thermal fluid.
  • FIG. 2 shows the roller body 1 in cross section AA.
  • the roller body 1 is a cast body. It is poured by gravity casting, for example in static chill casting, standing from a melt of an iron-based alloy. The central cavity is formed or incorporated later in this Urformung. As the iron-base alloy, a cast iron alloy is used. The cooling, which undergoes the melt primarily on the mold, is controlled so that the melt over the entire axial length of the roll body 1 from radially inward to radially outward to the outer circumference or almost to the outer circumference stably solidified in a ductile iron structure, ie in the form of a cast iron with nodular graphite.
  • the control of the cooling is done by customized design of the mold.
  • the cooling rate can be adjusted in particular via the radial thickness of the mold, the heat capacity of the mold, the thermal conductivity of the mold material or the total mass of the mold.
  • the mold can be designed only with respect to a single of said parameters or a combination of two, three or all four of these parameters by appropriate material selection and dimensioning.
  • the solidification process is controlled so that the melt solidly solidifies not only in an inner zone 5 surrounding the rotation axis R, but also in a peripheral edge zone 6 enclosing the inner zone 5, which forms the outer circumference of the roll body.
  • the roller body 1 thus solidifies over its entire cross-section stable and not white.
  • the carbon is eliminated in the stable solidification in the form of nodular graphite.
  • the directly obtained by the casting process roller body 1 thus has everywhere a ductile iron structure. Due to the cooling rate set deliberately by means of the mold, however, the graphite in the peripheral edge zone 1 separates out more finely than in the inner zone 5.
  • the graphite spherulites SG (sphero-graphite particles) of the peripheral edge zone 6 have a size in the range of the guide numbers of 5 to 8, ie a maximum dimension of at most 0.12 mm. More preferably, the cooling rate is set so that the graphite particles SG of the peripheral edge zone 6 have a size in the range of the guide numbers of 7 (0.022 microns) to 8 according to EN ISO 945, ie a maximum dimension of at most 0.03 mm.
  • the cast iron matrix is also in the peripheral edge zone 6 perlitic with at most a low ferrite content.
  • the pearlite content is at least 90%, more preferably at least 95%, and the ferrite content at most 10%, more preferably at most 5%. If carbide formation can not be prevented, the carbide content is less than 5%, more preferably less than 3%, not only in the inner zone 5 but also in the peripheral edge zone 6 solidified at a higher cooling rate.
  • FIG. 3 shows a part of the FIG. 2 and further, extracted, a further enlarged view of the microstructure of the roll body obtained by the casting.
  • These are the fineness of the excreted graphite particles SG
  • the microstructure shown next to the cross section of the roller body 1 are primarily schematic in nature, but qualitatively illustrate that the graphite particles SG in the peripheral edge zone 6 are smaller than the graphite particles SG in the inner zone 5 and in the peripheral edge zone 6 correspondingly in finer distribution.
  • the roll body 1 is made wear-resistant in its subsequent higher-hardness peripheral edge zone 6 already obtained by the casting in a subsequent hardening process.
  • the peripheral tempering 4 are incorporated, preferably drilled.
  • the peripheral edge zone 6 is understood to be that annular zone of the roller body 1 which, after hardening, has the hardness required for the respective application everywhere, ie extends from the outer circumference to the hardening depth. If the peripheral edge zone 6 of the hardened roll body 1 extends radially inwardly up to or even over the tempering channels 4, these are expediently incorporated before hardening. Otherwise, the tempering 4 can just as well be incorporated after curing.
  • the hardening process is carried out in such a way that the basic structure of the peripheral edge zone 6 obtained directly from the casting is converted into finely striated or, even more advantageously, finely striated perlite.
  • the graphite spherulites SG are thereby not or at least not changed in a manner relevant to the invention.
  • the hardening process can also be designed such that the cast iron matrix within the peripheral edge zone 6 is converted into an interstage structure, preferably in the form of austempered ductile iron (ADI).
  • ADI austempered ductile iron
  • the roll body 1 in the peripheral edge zone 6 is uniformly heated to a temperature in the austenitic region, for example at 950 ° C., and then quenched, the quenching rate for forming an interstage structure being set higher than for fine perlite transformation, but still not so big that a martensite transformation can take place.
  • the interstitial structure is similar to bainite, preferably the lower bainite, but is not bainite because it contains no or, for the desired strength, only negligible carbides. It is also true for the interstitial structure that the carbide fraction is advantageously less than 5%, preferably at most 3%. is. For the purposes of the invention, it would be ideal if neither the fine-pearlitic structure nor the alternative interstitial structure would contain carbides.
  • FIG. 4 illustrates a curing process using the example of the preferred induction hardening.
  • an induction device 8 and a quenching device 9 are moved axially from one end face of the roller body 1 to the other.
  • the movement is uniform with the speed v and a constant during the hardening process axial distance x, by which the induction device 8 precedes the quenching device 9.
  • the roller body 1 is uniformly heated to the predetermined hardening depth, ie within the peripheral edge zone 6, throughout the temperature range mentioned above and then quenched by means of the quenching device 9.
  • the quenching is preferably carried out with a liquid quenching fluid, for example water, which is injected onto the outer circumference of the roller body 1.
  • the peripheral edge zone 6 may in principle be heated by any other thermal surface treatment method as long as only the required temperature is adjusted with the required uniformity.
  • induction hardening in particular flame hardening comes into consideration, but primarily only for lower hardening depths. As hardening depth increases, induction hardening is the preferred choice.
  • the hardening depth and, accordingly, the thickness of the peripheral edge zone 6 are preferably at least 3 mm, more preferably at least 5 mm. On the other hand, it is advantageous in terms of thermal cycling, if the Einhärttiefe does not exceed 10mm.
  • the hardening depth can be influenced in particular by a variation of the distance x, in the case of induction hardening also by varying the frequency of the respective induction coil 8. Further adjusting parameters for influencing the hardening depth are the speed v, the choice of the Abschreekfluids and the throughput of quenching fluid.
  • FIGS. 5 and 6 are micrographs of the structure of the peripheral edge zone.
  • FIG. 5 shows the basic structure obtained directly from the casting in the scale 50: 1
  • FIG. 6 is a Micrograph of the microstructure after curing, thus showing the hardness structure, also in the scale 50: 1.
  • the graphite spheres or graphitic spherolites are denoted by SG, the perlite by P and ferrite islands by ⁇ .
  • the basic structure consists essentially of perlite and precipitated nodular graphite and small amounts of ferrite, less than 10% ferrite in the exemplary embodiment.
  • the hardness structure consists of fine-grained and very fine-grained pearlite, ie sorbitol and troostite, as well as the embedded sphero-graphite particles SG, the pearlite areas being designated S for sorbitol and T for troostite according to the fineness of the lamellae.
  • FIG. 7 the microhardness curve is shown for a given hardening depth of 3 mm, namely the hardness H in HV0.1 over the distance d from the outer circumference of the roll body 1, that is to say over the depth d.
  • the hardened roll body 1 is tempered, advantageously to a tempering temperature of between 300 and 350 ° C.
  • a particularly preferred iron-base alloy for casting the roll body 1 is specified in the last column of the table.
  • the second and third columns contain preferred ranges for the respective alloying partner, with the narrower ranges within the respective wider range being particularly preferred for the same alloying element.
  • the proportion specified in the last column is most preferred.
  • the iron-based alloy contains in a preferred embodiment at least carbon, silicon, copper and nickel within the respective specified ranges of shares. Copper as a perlite former and nickel to prevent martensite transformation are preferably used in combination. Fe makes up the rest of the respective alloy.
  • the iron base melt of the composition of the last column has a saturation degree Sc of 0.99 to 1.00. Preference is given to iron-base alloys having a degree of saturation Sc in the range from 0.97 to 1.03, from which range of alloys of near-tectic composition those having a degree of saturation Sc from the lower half of the stated range are preferred.
  • the roller body 1 of the embodiment is solidified in a nodular cast iron structure.
  • the embedded free graphite in the inner zone 5 and also in the peripheral edge zone 6 may be excreted substantially in the form of vermicular graphite or else in the form of spheroidal graphite and vermicular graphite.
  • the excretion of nodular graphite is given preference over the excretion of vermicular graphite.
  • the free graphite as nodular graphite and as Vermikulargraphit it is advantageous if the nodular graphite accounts for the majority of the free graphite.

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)
  • Rolls And Other Rotary Bodies (AREA)
  • Heat Treatment Of Articles (AREA)
  • Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
EP10150614.5A 2009-01-14 2010-01-13 Corps de cylindre pour un cylindre destiné au traitement d'un matériau et procédé de fabrication d'un corps de cylindre Active EP2213790B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE102009004562.7A DE102009004562B4 (de) 2009-01-14 2009-01-14 Walzenkörper für eine Walze zur Behandlung eines Materials und Verfahren zur Herstellung eines Walzenkörpers

Publications (2)

Publication Number Publication Date
EP2213790A1 true EP2213790A1 (fr) 2010-08-04
EP2213790B1 EP2213790B1 (fr) 2013-07-03

Family

ID=41719320

Family Applications (1)

Application Number Title Priority Date Filing Date
EP10150614.5A Active EP2213790B1 (fr) 2009-01-14 2010-01-13 Corps de cylindre pour un cylindre destiné au traitement d'un matériau et procédé de fabrication d'un corps de cylindre

Country Status (3)

Country Link
US (1) US8684895B2 (fr)
EP (1) EP2213790B1 (fr)
DE (1) DE102009004562B4 (fr)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100179039A1 (en) * 2009-01-14 2010-07-15 Shw Casting Technologies Gmbh Roller body for a roller for treating a material and method for manufacturing a roller body
EP2386660A1 (fr) * 2010-05-10 2011-11-16 SHW Casting Technologies GmbH Corps en fonte
EP2474665A1 (fr) * 2011-01-11 2012-07-11 SHW Casting Technologies GmbH Cylindre sec pour une machine à papier-tissu
WO2016012214A1 (fr) * 2014-07-23 2016-01-28 Voith Patent Gmbh Cylindre avec revêtement
WO2017016810A1 (fr) * 2015-07-28 2017-02-02 Siemens Aktiengesellschaft Procédé de fabrication d'un élément
WO2018072770A1 (fr) * 2016-10-18 2018-04-26 Reifenhäuser GmbH & Co. KG Maschinenfabrik Procédé de fabrication d'un rouleau de lissage, procédé de préparation d'une installation de lissage, rouleau de lissage et installation de lissage

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102010034529A1 (de) * 2010-08-16 2012-02-16 Man Diesel & Turbo, Filial Af Man Diesel & Turbo Se, Tyskland Teil oder Bauteil für Maschinen sowie Verfahren zur Herstellung eines solchen
CN103620265A (zh) * 2011-06-13 2014-03-05 Ntn株式会社 链条引导件和链条传动装置
JP5706261B2 (ja) * 2011-07-25 2015-04-22 Ntn株式会社 カム軸駆動用のチェーン伝動装置
FI123316B (fi) * 2011-10-18 2013-02-15 Metso Paper Inc Lämmönsiirtotela ja lämmönsiirtotelan valmistusmenetelmä
CN104169610B (zh) * 2012-03-12 2018-01-02 Ntn株式会社 链引导件以及链传动装置
US9400046B2 (en) * 2012-05-24 2016-07-26 Ntn Corporation Chain guide and chain transmission device
DE102012105163A1 (de) * 2012-06-14 2013-12-19 Andritz Küsters Gmbh Gravurwalzen-Herstellungsverfahren sowie Gravurwalze
JP6205291B2 (ja) * 2014-02-17 2017-09-27 Ntn株式会社 カム軸駆動用チェーン伝動装置
CN106367671B (zh) * 2016-08-31 2019-02-22 中钢集团邢台机械轧辊有限公司 一种适用于万能轧机的球墨铸铁轧边辊及其制造方法
JP6669109B2 (ja) * 2017-03-24 2020-03-18 Ｊｆｅスチール株式会社 熱間圧延用ロール外層材および熱間圧延用複合ロール
CN111168030B (zh) * 2020-02-04 2021-06-25 三鑫重工机械有限公司 一种含石墨的贝氏体半钢板带粗轧工作辊

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0505343A1 (fr) 1991-03-20 1992-09-23 Valmet Corporation Procédé pour la fabrication d'un rouleau et rouleau
EP0710741B1 (fr) * 1990-11-30 1999-12-08 S.D. Warren Company Procédé et appareil de calandrage pour papier
US20060037675A1 (en) * 2002-05-14 2006-02-23 Daniel Labbe Method for production and forming of cast pieces of spheroidal graphite with improved mechanical properties
WO2006072663A2 (fr) 2005-01-05 2006-07-13 Metso Paper, Inc. Fonte ductile et procede de fabrication associe pour l'elaboration de composants a proprietes de resistance et de tenacite desirees

Family Cites Families (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH211984A (de) * 1938-01-07 1940-10-31 Arnold Dr Locher Verfahren zur Verbesserung der mechanischen Eigenschaften von Gusseisen.
CH360701A (de) * 1957-09-19 1962-03-15 Tiroler Roehren & Metallwerk Verfahren zur Oberflächenhärtung von Gusseisen
US3065070A (en) * 1960-02-15 1962-11-20 Otani Kokichi Method for the manufacture of tough cast iron
US3411957A (en) * 1965-06-01 1968-11-19 Nisso Seiko Kabushiki Kaisha Method of manufacturing a cast iron roll
US3997370A (en) * 1975-11-17 1976-12-14 Bethlehem Steel Corporation Method of hot reducing ferrous and ferrous alloy products with composite martensitic nodular cast chill iron rolls
JPS60250815A (ja) * 1984-05-24 1985-12-11 Kubota Ltd 耐クラツク性及び耐摩耗性に優れた球状黒鉛鋳鉄カリバロ−ル及びその製造法
JPS61210151A (ja) * 1985-03-13 1986-09-18 Mazda Motor Corp 球状黒鉛鋳鉄鋳物
CH667285A5 (de) 1986-02-14 1988-09-30 Sulzer Ag Walze mit harter mantelflaeche.
JPH01152240A (ja) * 1987-12-10 1989-06-14 Toyota Motor Corp 高靭性鋳鋼
US4990194A (en) * 1988-09-09 1991-02-05 Hitachi Metals, Ltd. Thin high-strength article of spheroidal graphite cast iron and method of producing same
DE9000980U1 (fr) * 1990-01-29 1990-05-10 Schwaebische Huettenwerke Gmbh, 7080 Aalen, De
FI91297C (fi) * 1992-02-24 1994-06-10 Valmet Paper Machinery Inc Kuumennettava tela
DE4223359A1 (de) * 1992-07-16 1994-01-20 Escher Wyss Gmbh Heiz- oder Kühlwalze
US5611143A (en) * 1994-10-21 1997-03-18 Voith Sulzer Paper Technology North America, Inc. Process for making chilled iron rolls
JPH08215721A (ja) * 1995-02-09 1996-08-27 Nippon Steel Corp 圧延ロールの管理方法
FI2640U1 (fi) * 1996-03-22 1996-11-22 Valmet Corp Tela, erityisesti soft- tai superkalanterin tela
EP1217123B1 (fr) * 2000-12-08 2004-12-15 Walzen Irle GmbH Rouleau, en particulier rouleau pour calandre
ITMI20021670A1 (it) * 2002-07-26 2004-01-26 Erre Vis S P A Ghisa sferoidale particolarmente per la realizzazione di segmenti elastici di tenuta per pistoni di motori a combustione interna
DE102005051715A1 (de) * 2004-10-27 2006-05-18 Siempelkamp Giesserei Gmbh Verfahren zum Härten eines Gussteils
JP4787640B2 (ja) * 2006-03-17 2011-10-05 株式会社クボタ 圧延用複合ロール
JP5041938B2 (ja) * 2007-09-14 2012-10-03 株式会社クボタ 圧延用複合ロール
DE102009004562B4 (de) * 2009-01-14 2015-06-03 Shw Casting Technologies Gmbh Walzenkörper für eine Walze zur Behandlung eines Materials und Verfahren zur Herstellung eines Walzenkörpers
US20110274946A1 (en) * 2009-01-14 2011-11-10 Shw Casting Technologies Gmbh Cast body

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0710741B1 (fr) * 1990-11-30 1999-12-08 S.D. Warren Company Procédé et appareil de calandrage pour papier
DE69230413T2 (de) 1990-11-30 2000-05-25 S D Warren Co Verfahren und Vorrichtung zum Kalandern von Papier
EP0505343A1 (fr) 1991-03-20 1992-09-23 Valmet Corporation Procédé pour la fabrication d'un rouleau et rouleau
DE69219808T2 (de) 1991-03-20 1997-10-23 Valmet Corp Verfahren zum Herstellen einer Walze und Walze
US20060037675A1 (en) * 2002-05-14 2006-02-23 Daniel Labbe Method for production and forming of cast pieces of spheroidal graphite with improved mechanical properties
WO2006072663A2 (fr) 2005-01-05 2006-07-13 Metso Paper, Inc. Fonte ductile et procede de fabrication associe pour l'elaboration de composants a proprietes de resistance et de tenacite desirees

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100179039A1 (en) * 2009-01-14 2010-07-15 Shw Casting Technologies Gmbh Roller body for a roller for treating a material and method for manufacturing a roller body
US8684895B2 (en) * 2009-01-14 2014-04-01 Shw Casting Technologies Gmbh Roller body for a roller for treating a material and method of manufacturing a roller body
EP2386660A1 (fr) * 2010-05-10 2011-11-16 SHW Casting Technologies GmbH Corps en fonte
EP2474665A1 (fr) * 2011-01-11 2012-07-11 SHW Casting Technologies GmbH Cylindre sec pour une machine à papier-tissu
WO2016012214A1 (fr) * 2014-07-23 2016-01-28 Voith Patent Gmbh Cylindre avec revêtement
US10240291B2 (en) 2014-07-23 2019-03-26 Voith Patent Gmbh Roller with coating
WO2017016810A1 (fr) * 2015-07-28 2017-02-02 Siemens Aktiengesellschaft Procédé de fabrication d'un élément
WO2018072770A1 (fr) * 2016-10-18 2018-04-26 Reifenhäuser GmbH & Co. KG Maschinenfabrik Procédé de fabrication d'un rouleau de lissage, procédé de préparation d'une installation de lissage, rouleau de lissage et installation de lissage

Also Published As

Publication number Publication date
EP2213790B1 (fr) 2013-07-03
DE102009004562B4 (de) 2015-06-03
US8684895B2 (en) 2014-04-01
DE102009004562A1 (de) 2010-07-15
US20100179039A1 (en) 2010-07-15

Similar Documents

Publication Publication Date Title
EP2213790B1 (fr) Corps de cylindre pour un cylindre destiné au traitement d'un matériau et procédé de fabrication d'un corps de cylindre
DE69736020T2 (de) Stahlteil mit hohem Oberflächendruckwiderstand und entsprechendes Herstellungsverfahren
DE60305389T2 (de) Kugelgraphitgusseisen für Kolbenringe und Verfahren zu seiner Herstellung
DE102005060113B4 (de) Radlager sowie Verfahren zur Herstellung desselben
US20110274946A1 (en) Cast body
WO2001081643A1 (fr) Composant de roulement
DE102006017263A1 (de) Kurbelwelle und Verfahren zu deren Herstellung
DE69812269T2 (de) Verbundwalze zum kaltwalzen
DE60127925T2 (de) Hochfester Laufring und Verfahren zu seiner Herstellung
DE102016203022A1 (de) Verfahren zum Wärmebehandeln einer Stahllegierung
EP2192201B1 (fr) Acier à ressort, élément de ressort et procédé de fabrication d'un élément de ressort
EP2386660B1 (fr) Corps en fonte
DE69931601T2 (de) Stähle zum kaltschmieden und verfahren zu deren herstellung
EP1274872B1 (fr) Procede de production d'un acier allie a l'azote, compacte par pulverisation
EP4018006A1 (fr) Acier à outils pour applications de travail à froid et à grande vitesse
DE60037575T2 (de) Grosse lagerteile aus stahl
DE60027355T2 (de) Selbstschmierendes Kolbenringmaterial für Verbrennungsmotoren und Kolbenring
DE10062036C2 (de) Wälzlager und Verfahren zur Herstellung eines Bauteils eines Wälzlagers
DE60011115T2 (de) Stahlmaterial, dessen verwendung und herstellung
EP3088537A1 (fr) Procédé de production d'une fonte hpi
DE102004003541A1 (de) Stahl zur Verwendung in einer hochfesten Ritzelwelle und Herstellungsverfahren hierfür
DE69909940T2 (de) Teile aus martensitischem rostfreiem Stahl und Verfahren zu ihrer Herstellung
DE102005028588A1 (de) Brennkraftmaschine
DE2324750A1 (de) Herstellung von gehaertetem stahl
EP2354264B1 (fr) Substance active résistant à l'usure et à la chaleur, ainsi que son utilisation

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

17P Request for examination filed

Effective date: 20101006

17Q First examination report despatched

Effective date: 20101103

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 502010003836

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: D21G0001000000

Ipc: C21D0005000000

RIC1 Information provided on ipc code assigned before grant

Ipc: D21F 3/00 20060101ALI20121211BHEP

Ipc: C21D 9/38 20060101ALI20121211BHEP

Ipc: C21D 5/00 20060101AFI20121211BHEP

Ipc: C22C 37/04 20060101ALI20121211BHEP

Ipc: D21G 1/02 20060101ALI20121211BHEP

Ipc: D21F 3/08 20060101ALI20121211BHEP

Ipc: D21G 1/00 20060101ALI20121211BHEP

Ipc: C21D 5/02 20060101ALI20121211BHEP

Ipc: C22C 37/08 20060101ALI20121211BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

Ref country code: AT

Ref legal event code: REF

Ref document number: 619830

Country of ref document: AT

Kind code of ref document: T

Effective date: 20130715

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502010003836

Country of ref document: DE

Effective date: 20130829

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20130703

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20131104

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130904

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20131103

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20131003

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20131014

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20131004

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20140404

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502010003836

Country of ref document: DE

Effective date: 20140404

BERE Be: lapsed

Owner name: SHW CASTING TECHNOLOGIES G.M.B.H.

Effective date: 20140131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: LU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20140113

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140131

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140131

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20140930

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140131

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140131

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20140113

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20100113

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20170824

Year of fee payment: 10

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: AT

Payment date: 20180122

Year of fee payment: 9

Ref country code: IT

Payment date: 20180129

Year of fee payment: 9

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20130703

REG Reference to a national code

Ref country code: DE

Ref legal event code: R081

Ref document number: 502010003836

Country of ref document: DE

Owner name: HUETTENWERKE KOENIGSBRONN GMBH, DE

Free format text: FORMER OWNER: SHW CASTING TECHNOLOGIES GMBH, 73433 AALEN, DE

Ref country code: DE

Ref legal event code: R082

Ref document number: 502010003836

Country of ref document: DE

Representative=s name: SSM SANDMAIR PATENTANWAELTE RECHTSANWALT PARTN, DE

Ref country code: DE

Ref legal event code: R081

Ref document number: 502010003836

Country of ref document: DE

Owner name: SHW HIGH PRECISION CASTING TECHNOLOGY GMBH, DE

Free format text: FORMER OWNER: SHW CASTING TECHNOLOGIES GMBH, 73433 AALEN, DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 619830

Country of ref document: AT

Kind code of ref document: T

Effective date: 20190113

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20190113

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190113

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190113

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20190113

REG Reference to a national code

Ref country code: DE

Ref legal event code: R082

Ref document number: 502010003836

Country of ref document: DE

Representative=s name: SSM SANDMAIR PATENTANWAELTE RECHTSANWALT PARTN, DE

Ref country code: DE

Ref legal event code: R081

Ref document number: 502010003836

Country of ref document: DE

Owner name: HUETTENWERKE KOENIGSBRONN GMBH, DE

Free format text: FORMER OWNER: SHW HIGH PRECISION CASTING TECHNOLOGY GMBH, 89551 KOENIGSBRONN, DE

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FI

Payment date: 20240119

Year of fee payment: 15

Ref country code: DE

Payment date: 20240119

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20240119

Year of fee payment: 15