EP2386660B1 - Corps en fonte - Google Patents

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Publication number
EP2386660B1
EP2386660B1 EP11165452.1A EP11165452A EP2386660B1 EP 2386660 B1 EP2386660 B1 EP 2386660B1 EP 11165452 A EP11165452 A EP 11165452A EP 2386660 B1 EP2386660 B1 EP 2386660B1
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EP
European Patent Office
Prior art keywords
graphite
cast body
cast
iron
circumferential rim
Prior art date
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Active
Application number
EP11165452.1A
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German (de)
English (en)
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EP2386660A1 (fr
Inventor
Ulrich Severing
Bernd Eppli
Lutz Krodel-Teuchert
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SHW Casting Technologies GmbH
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SHW Casting Technologies GmbH
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Publication of EP2386660A1 publication Critical patent/EP2386660A1/fr
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    • 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
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/10—Cast-iron alloys containing aluminium or silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • 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
    • C21D2221/00—Treating localised areas of an article
    • C21D2221/10—Differential treatment of inner with respect to outer regions, e.g. core and periphery, respectively
    • 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
    • C21D5/04—Heat treatments of cast-iron of white cast-iron
    • C21D5/06—Malleabilising
    • C21D5/14—Graphitising

Definitions

  • the invention relates to a cast body, namely a tool for forming or forming a workpiece or a transmission member for transmitting force or torque to a workpiece contacting the original or forming tools, preferably a piston or plunger.
  • the tool or transfer member may be part of a press for forming or forming the workpiece or a forging tool.
  • the invention also relates to the tool or transfer member as such, prior to assembly with other components.
  • 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, in order to overcome the said drawbacks, that the roll body is cast from an iron-base alloy to form a pearlitic or ferritic-pearlitic microstructure 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.
  • the EP 2 213 790 A1 describes a roller body for a roller for treating a material, wherein the material of the peripheral edge zone of the roller body compared to the white cast iron has significantly improved strength values.
  • CH 360 701 A discloses a method for surface hardening of cast iron, in which the edge zone of a workpiece is converted into austenite by brief autogenous or induction heating and is then cooled relatively slowly.
  • 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.
  • Rolled bodies weigh many tons, for example, large roll bodies 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.
  • Ur- or forming devices in particular for forming metal workpieces are comparable.
  • Such tools and transfer members may be to act about stamps, dies, pistons and rams of presses and blacksmiths.
  • the cast body should have the required hardness on the surface and also 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 cast body which is cast from a single iron-based alloy.
  • the iron-base alloy forms an inner zone of gray cast iron, preferably nodular cast iron, in the cast body, and the inner zone encloses a peripheral edge zone containing the outer circumference of the cast body having a surface hardness greater than 400HV on the outer circumference, as has heretofore been prevalent Shell casting is the case.
  • the cast body can be seen in cross-section of full material, so that the inner zone of gray cast iron forms a central core of the cast body.
  • the casting may also be a hollow shell, so that the 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 castings with those of forged steel and avoids the risk of cracking associated with a martensite shell.
  • the cast body can be made significantly cheaper over its entire dimension in a cast and thus compared to a forged steel body.
  • the gray cast iron inner zone can be worked well, 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 hardness profile applied over the distance to the outer surface, corresponds at least to the hardness profile of conventional tools or transmission elements serving as master or forming 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 precipitation of the 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 nodular cast iron structure 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%. Percentages in% are always expressed as mass%, i. understood as% share of the respective 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 therefore the reduced micro-notch effect, the material of the peripheral edge zone of the cast body according to the invention significantly improved strength values compared to white cast iron.
  • the casting is a tool for or in a device for prototyping or forming workpieces, in particular metallic workpieces.
  • the cast body may for example form a punch or a die for plastic molding. Particularly advantageously, it can form a transmission element for transmitting force or torque to a tool which acts directly on the material during shaping.
  • Pistons and plungers of or for priming or forming devices are preferred examples.
  • Presses and forging tools, in particular with hydraulic force or torque transmission, are preferred examples of original and forming devices in which a cast body according to the invention can be used.
  • the cast body according to the invention is at least finished insofar as it no longer has to be subjected to thermal treatment and is preferably no longer subjected to it, which specifically serves to adjust the microstructure.
  • Any post-treatment for example a grinding or polishing, optionally a machining or, for example, a mechanical training and, in principle, thermal treatments that do not change in particular the claimed for the peripheral edge zone structure to such an extent that it no longer corresponds to the claimed invention, are, however, excluded.
  • a method for producing the cast body comprises at least the following steps: the cast body is cast from a melt of an iron-based alloy, so that the melt is stable as cast iron both in the inner zone of the cast body and in the outer peripheral and reaching to the outer periphery peripheral edge zone and 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 solidifies.
  • 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 cast body obtained with this cast structure is formed by means of a thermal surface treatment on the outer periphery, 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. Chill casting can be static or instead dynamic, ie centrifugal casting.
  • the cast body is expediently poured upright, that is to say with a main axis in a vertical orientation. Casting against mold permits a more precise setting of the cooling rate, in particular via the choice of the thickness of the mold, the specific or the absolute, measured radially to the main axis of the cast body Heat capacity, the thermal conductivity or the mass of the mold or a suitable combination of such parameters on the part of 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 , Using a mold of lower thermal conductivity, lower mold mass, in each case in comparison with a mold for casting a cast 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 explained above for the preferred spheroidal graphite nodular graphite is excreted in the peripheral edge zone in graphite spheres 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 in the size range between 7 and 8 according to EN ISO 945, ie in the guideline 7/8 before.
  • 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.
  • the cast body is hardened to a depth of advantageously at least 3 mm, preferably at least 5 mm, by the cast iron matrix being converted into the fine-grained or extremely fine-grained pearlite or the interstitial microstructure up to at least this hardening depth.
  • a hardening depth of 7 mm is optimal.
  • a hardening depth of more than 10 mm should not be ruled out, large hardening depths produce material stresses in the event of a temperature change, with the risk that the hardened layer, the circumferential edge zone, will flake off.
  • Flame hardening and induction hardening are particularly suitable as methods of thermal surface treatment, with induction hardening preference is given to the fact that flame hardening is limited to the lower part of the hardening depth, generally still below 3 mm. Flame hardening is therefore primarily for castings 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 cast body is advantageously tempered to relieve stress.
  • the tempering temperature is above the temperature that reaches the cast body in later operation at the most, advantageously above 300 ° C, preferably a tempering temperature in the range of 300 to 350 ° C. Even after such tempering, the cast body in the peripheral edge zone has the fine or very fine-grained pearlitic structure with spherical or vermicular graphite or the interstitial 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 perlitizer, and having 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.
  • Manganese and tin are also preferred alloying agents, manganese preferably from 0.3 to 0.45%, tin preferably from 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 cast body 1, namely a roller body, 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 cast 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 cast body 1 pass through from one axial end to the other, continuous, near the outer periphery of the cast body 1 located, peripheral tempering 4, which are flowed through during the thermal treatment of the material of the thermal fluid.
  • FIG. 2 shows the cast body 1 in cross section AA.
  • a central cavity is continuously formed axially.
  • the cast body 1 is poured in a chill 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 experiences the melt primarily on the mold, is controlled so that the melt solidifies over the entire axial length of the cast body 1 from radially inward to radially outward to the outer circumference or almost to the outer circumference stably 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 only with respect to a single of the mentioned parameters or a combination be designed by 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 cast body.
  • the cast 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 cast body 1 immediately obtained by the casting process thus has everywhere a nodular cast 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 casting obtained by the casting.
  • These are the different microstructures of the inner zone 5 and the peripheral edge zone 6 with respect to the fineness of the precipitated graphite particles SG.
  • the microstructure shown next to the cross section of the cast body 1 are primarily of a schematic nature, but qualitatively illustrate that the graphite particles SG are in the peripheral edge zone 6 are smaller than the graphite particles SG in the inner zone 5 and present in the peripheral edge zone 6 correspondingly in finer distribution.
  • the cast 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 circumferential edge zone 6 is that annular zone of the cast 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 cast 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 so that the cast iron matrix within the peripheral edge zone 6 converts into an interstage structure, preferably in austempered ductile iron (ADI).
  • ADI austempered ductile iron
  • the cast body 1 is heated uniformly in the peripheral edge zone 6 to a temperature in the austenitic region, for example at 950 ° C, and then quenched, wherein the quenching rate for the formation of an interstage structure is set higher than for the transformation into the fine perlite, 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%. 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 cast 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 induction device 8 surrounds the cast body 1 by means of the induction device 8 up to the predetermined hardening depth, ie within the peripheral edge zone 6, uniformly throughout the temperature range 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 cast 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. With increasing depth of cure, induction hardening is the preferred choice.
  • the Einhärttiefe and, accordingly, the thickness of the peripheral edge zone 6 is preferably at least 3mm, more preferably at least 5mm. 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 quenching fluid 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 microsection of the structure after hardening, thus showing the hardness structure, also in 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 at a given hardening depth of 3 mm, namely the hardness H in HV0.1 over the distance d from the outer circumference of the cast body 1, that is to say over the depth d.
  • the hardened cast body 1 is tempered, advantageously to a tempering temperature between 300 and 350 ° C.
  • a particularly preferred iron-base alloy for casting the cast 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.
  • FIG. 8 shows a hydraulic press with a cast body 10 according to the invention, which forms a piston of the press.
  • the cast body 10 is guided in a cylinder 11 of the press along a working axis A back and forth.
  • a forming tool 12 for example a stamp, is arranged on a front side of the cast body 10.
  • the press has the die 12 axially opposite a die 13.
  • the cylinder 11 forms at the back of the casting 10 a pressure space with an inlet 14 and an outlet 15 for a hydraulic working fluid to the casting 10 for molding workpieces with a working pressure P of more than 100 bar, preferably at least 200 bar, in direction to be able to act on the die 13.
  • FIG. 9 shows a casting 10 with a modified form.
  • the modified cast body 10 may also be used as a piston of a press, preferably a hydraulic press. While the cast body 10 of the previous embodiment is at least substantially cylindrically shaped, the modified cast body 10 is at least substantially in the shape of a pot with a bottom forming the back of the piston and a side wall.
  • the cast bodies 10 each have a microstructure corresponding to the cast body 1 with a gray-solidified inner zone 5 and an outer peripheral edge zone 6, which encloses the inner zone 5 over the circumference and preferably also over the end faces.
  • the pot-shaped cast body 10 has a peripheral edge zone 6 according to the invention, as also preferably on that outer peripheral surface which rotates on the inside and preferably also on the end face located in the pot.
  • a peripheral edge zone 6 according to the invention preferably encloses the respective cast body 10 on all sides. For the zones 5 and 6 of the cast body 10, the statements made on the zones 5 and 6 of the cast body 1 apply.
  • the cast bodies 1 and 10 are each 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 is present as spheroidal graphite and also as Vermikulargraphit, it is advantageous if the spheroidal graphite makes up the vast majority of the free graphite.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)

Claims (15)

  1. Corps en fonte, notamment outil pour le formage ou la déformation d'une pièce ou organe de transmission (10) pour la transmission d'une force ou d'un couple de rotation à un outil (12) en contact avec la pièce lors du formage ou de la déformation, dans lequel le corps en fonte n'est pas un rouleau et
    a) est coulé en un alliage à base de fer,
    b) qui forme une zone intérieure (5) du corps en fonte (10) en fonte grise (GJS, GJV) et
    c) autour de la zone intérieure (5) une zone périphérique (6) contenant la périphérie extérieure du corps en fonte (1)
    d) avec une dureté de surface supérieure à 400 HV,
    e) dans lequel la zone périphérique (6) se compose de perlite à lamelles fines ou très fines (P) avec du graphite interstitiel libre, 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.
  2. Corps en fonte selon la revendication précédente, caractérisé en ce que le graphite interstitiel libre 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 nombre indicatif d'au moins 5, de préférence d'au plus 7, selon la norme EN ISO 945.
  3. Corps en fonte selon l'une quelconque des revendications précédentes, caractérisé en ce que la fonte contient dans la zone périphérique (6) au moins 95% de perlite et au plus 5 % de ferrite.
  4. Corps en fonte selon l'une quelconque des revendications précédentes, 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 % Rp,02 > 400 N/mm2;
    (ii) résistance à la traction Rm > 600 N/mm2, de préférence Rm > 650 N/mm2;
    (iii) allongement à la rupture A > 1,5 %, de préférence A > 2 %.
  5. Corps en fonte selon l'une quelconque des revendications précédentes, caractérisé en ce que le corps en fonte (10) est un composant d'un outil de forgeage ou d'une presse pour la déformation ou le formage de la pièce.
  6. Corps en fonte selon l'une quelconque des revendications précédentes, caractérisé en ce que le corps en fonte (10) est un piston ou un poussoir, de préférence destiné à l'application d'une force hydraulique.
  7. Corps en fonte selon l'une quelconque des revendications précédentes et présentant au moins une des caractéristiques suivantes:
    (i) l'alliage à base de fer contient au moins 0,3 % de Ni, de préférence au plus 1,5 % de Ni;
    (ii) l'alliage à base de fer contient au moins 0,5 % de Cu, de préférence au plus 1,3 % de Cu.
  8. Corps en fonte selon l'une quelconque des revendications précédentes, caractérisé en ce que l'alliage à base de fer contient au moins 1,7 % de Si, de préférence au plus 2,4 % de Si.
  9. Corps en fonte selon l'une quelconque des revendications précédentes, caractérisé en ce que l'alliage à base de fer contient 3 - 4 % de C.
  10. Procédé de fabrication d'un corps en fonte selon l'une quelconque des revendications précédentes, dans lequel:
    a) on coule contre un moule le corps en fonte (1; 10) à partir d'une masse fondue d'un alliage à base de fer;
    b) on règle la vitesse de refroidissement sur le moule à un niveau tellement bas que la masse fondue se solidifie non en fonte blanche même dans une zone périphérique (6) contenant la périphérie extérieure du corps en fonte (1; 10), mais en fonte stable (GJS, GJV) avec du graphite interstitiel libre, 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 de surface en perlite à lamelles fines ou très fines (P) avec du graphite sphéroïdal ou vermiculaire (SG, V) ou en une structure intermédiaire (ADI) avec du graphite sphéroïdal ou vermiculaire.
  11. Procédé selon la revendication précédente, caractérisé en ce que le graphite interstitiel libre de la zone périphérique (6) est au moins essentiellement du graphite sphéroïdal (SG) et on règle la vitesse de refroidissement sur le moule à un niveau tel que les sphères de graphite de ce graphite sphéroïdal (SG) dans la zone périphérique solidifiée (6) présentent une taille, qui correspond à un nombre indicatif d'au moins 5, de préférence d'au plus 7, selon la norme EN ISO 945.
  12. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que la fonte dans la zone périphérique (6) contient au moins 90 % de perlite et au plus 10 % de ferrite avant le traitement de surface.
  13. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'alliage à base de fer est composé d'une manière telle que la température de début de transformation martensitique (Ms) de la fonte soit inférieure à 20°C.
  14. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'on effectue le traitement de surface sans transformation martensitique.
  15. Procédé selon l'une quelconque des revendications précédentes, caractérisé en ce que l'on soumet le corps en fonte (1; 10) à un revenu après l'exécution d'un traitement de surface et on le refroidit de nouveau sans transformation martensitique.
EP11165452.1A 2010-05-10 2011-05-10 Corps en fonte Active EP2386660B1 (fr)

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DE102018209267A1 (de) 2018-06-11 2019-12-12 Federal-Mogul Nürnberg GmbH Kolben für Verbrennungsmotoren und Verwendung eines Kolbens für Verbrennungsmotoren
CN109227046A (zh) * 2018-10-18 2019-01-18 南通重矿金属新材料有限公司 一种孔型样板的制作方法
CN115962231B (zh) * 2023-01-16 2023-06-27 泰尔重工股份有限公司 一种一体式万向联轴器法兰叉头及其制作方法

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CH360701A (de) * 1957-09-19 1962-03-15 Tiroler Roehren & Metallwerk Verfahren zur Oberflächenhärtung von Gusseisen
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
FI88420B (fi) 1991-03-20 1993-01-29 Valmet Paper Machinery Inc Foerfarande foer framstaellning av en vals och en vals
JP3050368B2 (ja) * 1995-10-18 2000-06-12 トヨタ自動車株式会社 プレス成形用一体金型の製造方法
JP3204293B2 (ja) * 1996-04-29 2001-09-04 日立金属株式会社 球状黒鉛鋳鉄部材の製造方法
JP4526616B2 (ja) * 1999-06-01 2010-08-18 高周波熱錬株式会社 球状黒鉛鋳鉄材からなる歯車およびその製造方法
FI118738B (fi) * 2005-01-05 2008-02-29 Metso Paper Inc Pallografiittivalurauta ja menetelmä pallografiittivaluraudan valmistamiseksi lujuutta ja sitkeyttä vaativia koneenrakennusosia varten
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

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ITMI20110150U1 (it) 2011-11-11
DE202010006651U1 (de) 2010-08-05

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