EP2213790B1 - 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 PDFInfo
- Publication number
- EP2213790B1 EP2213790B1 EP10150614.5A EP10150614A EP2213790B1 EP 2213790 B1 EP2213790 B1 EP 2213790B1 EP 10150614 A EP10150614 A EP 10150614A EP 2213790 B1 EP2213790 B1 EP 2213790B1
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- EP
- European Patent Office
- Prior art keywords
- graphite
- roller body
- roller
- circumferential rim
- zone
- Prior art date
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 46
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 28
- 229910045601 alloy Inorganic materials 0.000 claims description 27
- 239000000956 alloy Substances 0.000 claims description 27
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- 229910052742 iron Inorganic materials 0.000 claims description 19
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- 238000004381 surface treatment Methods 0.000 claims description 12
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- 239000000470 constituent Substances 0.000 claims 1
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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 DE 692 19 808 T2 describes a method of making a roll having an inner part and a surface hardened layer.
- the inner part has a pearlitic or ferritic-pearlitic structure, while the surface layer of the roller after the surface hardening is occasion martensitic.
- WO 2006/072663 A2 discloses the production of a cast iron with nodular graphite.
- the cast iron is used for engineering components which require high strength and toughness.
- the roll is made of a first material of forged steel, cast steel, cast iron or spheroidal graphite cast iron and provided with a thin circumferential surface layer of a second hard abrasion resistant material.
- 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 of either fine-grained or very fine-grained perlite with vermicular graphite or preferably spheroidal graphite or of an interstage structure, preferably ADI with spherical or vermicular graphite, and is free of martensite.
- 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 graphite nodules.
- 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 transformation 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 completely 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.
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Claims (14)
- Corps de cylindre pour un cylindre destiné au traitement d'un matériau, de préférence d'un matériau en bande, quia) est coulé en un alliage à base de fer,b) forme une zone radialement intérieure (5) du corps de cylindre (1) en fonte grise (GJS, GJV) etc) autour de la zone intérieure (5) une zone périphérique (6) contenant la périphérie extérieure du corps de cylindre (1),d) avec une dureté superficielle supérieure à 400 HV,e) dans lequel la zone périphérique (6) se compose de perlite fine ou lamellaire fine (P) avec du graphite libre incorporé, de préférence du graphite sphéroïdal (SG) ou du graphite vermiculaire (V), ou d'une structure intermédiaire (ADI) avec du graphite sphéroïdal ou du graphite vermiculaire et est libre de martensite.
- Corps de cylindre selon la revendication précédente, caractérisé en ce que le matériau de la zone périphérique (6) présente au moins une des valeurs de résistance suivantes:(i) limite d'élasticité à 0,2 % R0,02 > 400 N/mm2,(ii) résistance à la traction Rm > 600 N/mm2, de préférence Rm > 650 N/mm2,(iii) allongement de rupture A > 1,5 %, de préférence A > 2 %.
- Corps de cylindre selon l'une quelconque des revendications précédentes, caractérisé en ce que le graphite libre incorporé est au moins essentiellement du graphite sphéroïdal (SG) et les sphères de graphite de ce graphite sphéroïdal présentent dans la zone périphérique solidifiée (6) une taille qui correspond à un chiffre d'au moins 5, et d'au plus 7, selon la norme EN ISO 945.
- Corps de cylindre selon l'une quelconque des revendications précédentes, caractérisé en ce que le corps de cylindre (1) présente des perçages périphériques (4) répartis autour de son axe longitudinal central (R) pour le passage d'un fluide thermique.
- Corps de cylindre selon l'une quelconque des revendications précédentes, caractérisé en ce que le corps de cylindre (1) est un composant du cylindre et des flasques à tourillon (2, 3) sont fixés aux extrémités axiales du corps de cylindre (1) pour un appui rotatif du cylindre.
- Procédé de fabrication d'un corps de cylindre, de préférence selon l'une quelconque des revendications précédentes, dans lequel:a) on coule le corps de cylindre (1) à partir d'un bain fondu d'un alliage à base de fer contre une lingotière,b) on règle une faible vitesse de refroidissement dans la lingotière, de telle manière que le bain fondu ne se solidifie pas sous forme blanche, même dans une zone périphérique (6) contenant la périphérie extérieure de corps de cylindre (1), mais sous forme stable comme fonte (GJS, GJV) avec du graphite librement incorporé, de préférence du graphite sphéroïdal (SG) ou du graphite vermiculaire (V),c) et on transforme le matériau de la zone périphérique (6), au moyen d'un traitement thermique superficiel, en perlite fine ou lamellaire fine (P) avec du graphite sphéroïdal ou vermiculaire (SG, V) ou en une structure intermédiaire (ADI) avec du graphite sphéroïdal ou vermiculaire,d) dans lequel on chauffe la zone périphérique brièvement dans le domaine austénitique, en fonction de la dureté superficielle et de la profondeur de trempe, de préférence à au moins 880°C et de préférence encore à environ 950°C,e) et on refroidit le matériau chauffé avec une vitesse de refroidissement, pour laquelle on évite la transformation martensitique.
- Procédé selon la revendication précédente, dans lequel l'alliage à base de fer contient au moins 0,3 % de Ni, de préférence au plus 1,5 % de Ni.
- Procédé selon l'une quelconque des revendications précédentes, dans lequel l'alliage à base de fer contient au moins 0,5 % de Cu, de préférence au plus 1,3 % de Cu.
- Procédé selon l'une quelconque des revendications précédentes, dans lequel l'alliage à base de fer est composé d'une manière telle que la température de début de la transformation martensitique (Ms) de la fonte soit inférieure à 20°C.
- Procédé selon l'une quelconque des revendications précédentes, dans lequel le graphite libre incorporé de la zone périphérique solidifiée (6) est du graphite sphéroïdal (SG) et on règle une vitesse de refroidissement à la lingotière, à une valeur telle que les sphères de graphite de ce graphite sphéroïdal (SG) dans la zone périphérique solidifiée (6) présentent une taille qui correspond à un chiffre d'au moins 5, de préférence d'au plus 7, selon la norme EN ISO 945 de septembre 1994 (N° de réf. DIN EN ISO 945:1994-09).
- Procédé selon l'une quelconque des revendications précédentes, dans lequel la fonte dans la zone périphérique (6) contient, avant le traitement superficiel, au moins 90 % de perlite et au plus 10 % de ferrite.
- Procédé selon l'une quelconque des revendications précédentes, dans lequel la fonte dans la zone périphérique (6) contient, après le traitement superficiel, au moins 95 % de perlite et au plus 5 % de ferrite.
- Procédé selon l'une quelconque des revendications précédentes, dans lequel l'alliage à base de fer contient au moins 1,7 % de Si, de préférence au plus 2,4 % de Si.
- Procédé selon l'une quelconque des revendications précédentes, dans lequel l'alliage à base de fer contient 3 - 4 % de C.
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DE102009004562.7A DE102009004562B4 (de) | 2009-01-14 | 2009-01-14 | Walzenkörper für eine Walze zur Behandlung eines Materials und Verfahren zur Herstellung eines Walzenkörpers |
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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 |
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US (1) | US8684895B2 (fr) |
EP (1) | EP2213790B1 (fr) |
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CN106367671A (zh) * | 2016-08-31 | 2017-02-01 | 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 |
CN111168030A (zh) * | 2020-02-04 | 2020-05-19 | 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 |
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DE202010006651U1 (de) * | 2010-05-10 | 2010-08-05 | Shw Casting Technologies Gmbh | Gusskörper |
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 |
DE202011001325U1 (de) * | 2011-01-11 | 2011-03-10 | Shw Casting Technologies Gmbh | Trockenzylinder für eine Tissue-Papiermaschine |
EP2719922A4 (fr) * | 2011-06-13 | 2015-04-08 | Ntn Toyo Bearing Co Ltd | Guide chaîne et appareil d'entraînement de chaîne |
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 |
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CN104321559B (zh) * | 2012-05-24 | 2017-08-25 | Ntn株式会社 | 链条引导件以及链条传动装置 |
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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 |
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-
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CN106367671A (zh) * | 2016-08-31 | 2017-02-01 | 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 |
CN111168030A (zh) * | 2020-02-04 | 2020-05-19 | 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 |
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US20100179039A1 (en) | 2010-07-15 |
EP2213790A1 (fr) | 2010-08-04 |
DE102009004562B4 (de) | 2015-06-03 |
DE102009004562A1 (de) | 2010-07-15 |
US8684895B2 (en) | 2014-04-01 |
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