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    • 专利摘要:
    Ring-shaped tool (1) having at least one radially outwardly directed working area (4) with high wear resistance and an axially closer tensioner (5), the person skilled in the art as a rocking bit for rock or as a cutting ring, in particular for tunnel boring machines, known, made of a material which an iron-based alloy is formed as a matrix with embedded hard material particles, w the hard material particles of carbide and / or nitride and / or oxide and / or boride, optionally as carbonitride or oxycarbonitride with boron at least one of the elements, or in a mixed form of the elements, the groups 4 and 5 of the periodic table, are gebied and have a density at room temperature of greater than 7400 kg / ma, preferably greater than 7600 kg / m ", and a method for its preparation.
    公开号:AT514133A1
    申请号:T300/2013
    申请日:2013-04-12
    公开日:2014-10-15
    发明作者:Bernhard Feistritzer
    申请人:Bernhard Feistritzer；
    IPC主号:
    专利说明:

    • ················································ •·· ·······
    Ring-shaped tool
    The invention relates to an annular tool with at least one radially outwardly directed working area with high wear resistance and an axially closer clamping part, known to those skilled as a roller chisel for rock or as a cutting ring, in particular for tunnel boring machines.
    The invention further relates to a method for producing annular tools having at least one radially outwardly directed working area and an axially closer clamping part, known to the skilled person as a roller cutter or cutting ring, formed from an iron-based alloy as a matrix, in which hard material particles, such as carbides and / or nitrides and / or carbonitrides and / or borides, if appropriate embedded in a mixed form of the elements of groups 4 and / or 5 of the periodic table.
    State of the art
    Drilling rigs for rock formations or rock and the like, are usually equipped for larger diameter with annular tools, which have an outwardly directed working area and roll under pressure on the rock bottom and thereby cause a removal or a break of this.
    Tunnel boring machines, for example, have a large dish-shaped tool holder, in which a plurality of so-called roller bits or cutting rings are mounted rotatably mounted. When propulsion of the tool holder is rotated and pressed with high force to the mountains, the same on different radii arranged roller bits in the respective areas rock are effectively breaking and the excavated rock or the so-called cuttings is discharged behind the tool holder.
    In accordance with the mechanical requirements, the annular tool is intended to be provided with a tapered, radially outward-pointing 2/25 ···· ··· ··· ·····································································. ····· »· · · · · · · · · · · ···
    Work area, in this particular high wear resistance and high hardness and high toughness of the material have.
    In most cases, the tool raw part is shrunk onto an axis, wherein tensile stresses inevitably arise in the clamping region, which are superimposed in the heavy, the hard rock breaking operation, respectively the required compressive stresses of the material and do not result in substantially stationary loads of the tool material. 10 roller bits should therefore have a working area with the highest possible
    Wear resistance and a clamping range with sufficiently high hardness and high toughness and overall have a superior resistance to fracture of the material with varying mechanical stress, because a failure of a tool causes costly repair work with a standstill of iS drill.
    The cutting rings are usually made of a tool steel. The shaping is generally carried out by a forging process, wherein the desired material properties are achieved by a subsequent heat treatment 20. The skilled person is aware that the greatest possible
    Wear resistance of tool steels can only be achieved with a high hardness of the microstructure. Here it must be accepted that with increasing hardness the tenacity of the structure decreases. In order to achieve the best properties for tool steels in terms of hard use as a cutting ring, a compromise between maximum wear resistance and high toughness must be made.
    Various attempts have been made to extend the life of the cutting rings by combining extremely wear-resistant materials with tough but tough materials. DE 10 2005 039 036 B3 describes, for example, a steel roller chisel which has welded segments in the working area, these tungsten carbide hard metal particles containing. From JP 2000001733 A, a similar cutting ring is known, which is a 3/25 2 · «* · * ·· * ··· ··· ···
    Outside circumference on a base made of nodular cast iron applied Martmetallring has. Furthermore, from the writings JP 2007138437 A, GB 1188305, GB 1379151, DE10300624A1 and DE 101 61 825 A1 cutting rings for tunnel boring machines are known, which have arranged on the outer circumference segments, 5 or cylindrical and otherwise specially shaped parts made of hard metal, which by soldering , Pressing or pouring be connected to the body. CA 2 512 737 A1 also describes a cutting ring in which segments made of hard metal are axially clamped between two disks. All of these known approaches to solutions involve either a very complex and complicated production or lead for example by high thermal stresses during use or by the softening of the solder for early failure of the cutting rings in use. JP 59144568 A describes a production method for cutting rings in which a melt containing tungsten carbide-based cemented carbide particles is poured into a rotating mold, whereupon the hard metal particles concentrate in the outer region of the cast body added hard metal particles are partially dissolved by the melt and can form unwanted, brittle microstructural constituents in the structure of the tool during solidification. Also, the minimum size of the added 20 cemented carbide particles is limited by the dissolution process.
    Object of the invention
    The invention has for its object to provide a generic, annular tool, which allows an increased operating time in hard, rock-breaking operation. 30 Furthermore, it is an object of the invention to provide a method of the type mentioned for the production of annular tools, which according to the respective stresses have an optimal material structure. 4/25 3: ··· »». : ·, Γ ·: φ: * ♦ ················································
    The above-mentioned object to provide a generic, annular tool, which allows an increased service life in hard, rock-breaking operation, is achieved by the tool consists of a material which is formed from an iron-based matrix alloy with incorporated in this hard particles 5. The hard material particles may be formed of carbide, nitride, oxide or boride, but also as compounds of these, such as carbonitride, carboboride or Qxikarbonitrid with boron. Depending on the application, it may be advantageous that mixtures of these different types of hard materials are included in the tool. The proportion of metal in the hard material particles essentially comes from Groups 4 and 5 of the Periodic Table (Ti, Zr, Hf, V, Nb, Ta), whereby here too only individual elements from these groups or mixtures thereof can be contained in the hard materials , Compared to the hard steels frequently used in iron metallurgy, the metallic components of which come from group 6 of the periodic table (eg tungsten carbide), hard materials of 15 metals of groups 4 and 5 have the advantage that they are found in the usual melting and casting temperatures of iron-based alloys have up to 1650 ° C only a low solubility in a molten iron melt.
    It is known that hard substances which are formed or precipitated during the solidification of a base melt and during the further cooling of the resulting workpiece preferably form eutectic microstructures or precipitate at grain boundaries. The hard materials thus formed can significantly reduce the toughness of the structure. The advantage of the low solubility of the above hard materials in a molten iron melt lies in the fact that on the one hand large quantities of these hard materials can be contained as solid particles in the melt, while on the other hand only small amounts are present during the solidification of the melt and during the further cooling of the workpiece additional hard material particles are formed or eliminated in the microstructure. These small amounts of brittle hard materials negatively affect the toughness of the 3o structure only to a small extent. However, these can increase toughness even when the precipitated particles are sufficiently fine to reduce grain growth of the matrix during heat treatment. 5/25 5 * '· ················································································································································································································· * '. »» · · · · · 4 «» · · «* · · · · · · * ·
    In order to achieve a high wear resistance and long service life of the roller chisel, both a minimum proportion of hard material particles in the structure should be present, as well as the Hartstöffteilchen be distributed inhomogeneous in the cutting ring so that a high proportion of these in the radially outward working area of
    Roller chisel is located. For a volume fraction of the wear-resistant working range of about 8% by volume (% by volume) considered sufficient, a hard material portion of at least 5% by volume, in each case based on the entire workpiece, has proven suitable. At least 8% by volume of hard particles are necessary when heavy duty cutting ring conditions are used. The possible service life of the roller bits can be increased with a larger volume fraction of the working area. Thus, the proportion of the work area can be increased to about 25% by volume and above, to allow long operating times in difficult operating conditions. iS The desired distribution of the hard material particles in the cutting ring is achieved if their density is higher than the density of the melt and they thus move outward in the centrifugal casting process. Experiments have shown that good results are already achieved if the density of the hard material particles at room temperature is greater than 7400 kg / m3. A desired, high concentration of the hard material ponds in the working area is achieved if these have a density greater than 7600 kg / m 3 at room temperature. Hard materials with this density are, for example, carbides, nitrides and carbonitrides of niobium, which have proven themselves in tests. It has also been shown that a slight addition of vanadium to these niobium hard materials can favorably influence the growth and the properties of the particles, but with the addition of vanadium the density of the particles decreases. A ratio of Nb atom% / V atom% > 5 should be complied with in any case niobium-vanadium mixed carbides, which may optionally be carbonitrides. Higher concentrations of these particles in the working range are given with a ratio Nb atom% / V atom% > 10 reached.
    It is known to the person skilled in the art that the wear resistance of a microstructure depends not only on the hardness of the matrix and the incorporated hard material particles, but also on their quantitative ratio, but also on the size distribution of the microstructure. •: ·:. :::::: »» '#', ·: ·: · · · · ·
    Hard material particle depends. In the following, all structural constituents are understood as a matrix, which are not the abovementioned hard substance constituents. If the particles of hard material are too small, they can be removed from the matrix in the form of entire particles as a result of their fearsome wear, without increasing their wear resistance, in particular 5. However, if the particles are too large, they may break under the high pressure load during the rock-breaking operation and thereby also not increase the wear resistance sufficiently. In the present case of the roller bits it has been found that best results can be achieved if at least 60% by volume, preferably at least 75% by volume, of the hard material particles having a size of less than 70 μm are formed.
    In addition to the properties of the hard particles, the properties of the matrix are of crucial importance in order to achieve high wear resistance in the work area of the roller bits. In particular, the properties of the matrix iS crucial to allow a sufficient toughness of the structure both in the work area, as well as in the clamping range. The properties of the matrix are mainly based on their chemical composition and possible heat treatment. Carbon is the most important alloying element and, above all, affects the hardenability of the steel, with about 20 0.28% C being considered as the lower limit for sufficient hardenability of the steel for the present application. With a carbon content of more than 1.2% in the matrix, a carbide network can form in the structure which reduces its toughness. Silicon increases the strength and wear resistance but also the melt pourability, but should not exceed 2% in the matrix. Manganese sets the critical
    Cooling rate down to the formation of the martensite and allows with sufficient amount of up to 2%, an air hardening of the cutting rings. Higher manganese contents of up to 25% can significantly increase the solubility of carbon in austenite and influence the austenite transformation properties during cooling or mechanical stress. at
    Manganese content up to 25%, the carbon content in the matrix can also be up to 2.3%. Like manganese, chromium also increases the hardenability of the steel and forms secondary and tertiary carbides which are precipitated from the austenite 7/25 6 • r · · · · · · · · · · · · · · · · · · · · · · · And increase the wear resistance, whereby excessively high chromium contents lead to a chromium carbide network in the microstructure. English:. German: v3.espacenet.com/textdoc , The chromium content should therefore not be higher than 6.0%. Like manganese and chromium, nickel also promotes martensite formation and, in addition, increases the toughness of the matrix. For nickel, a content of 2.5% appears to be sufficient as the upper limit in the matrix to achieve the necessary properties. To set a low critical cooling rate, a combination of Mn, Cr and Ni has been demonstrated. Molybdenum increases the strength of the matrix up to about 2.2% and increases the wear resistance through the formation of carbides. Tungsten forms together with Nb and ίο V mixed carbides as well as mixed nitrides and can thus increase the density of these hard materials. However, the content of W in the melt is adjusted so that after ejection of the primary hard materials formed in the matrix only a content of max. 1.5%, since otherwise a network of W-Mo mixed carbides may be formed together with Mo. For this reason, 1.5xMo + W i5 should not be more than 3.5%. Due to the high affinity of Nb and V to C or N of these in the matrix remain only small amounts of less than max. 0.8% back.
    Like Nb and V, Ti, Zr, Hf, and Ta also remain low in the matrix. Cobalt may be present in the matrix to increase the high temperature strength of cutting rings of up to 3% in the matrix. For the deoxidation of the melt is often added AI, which after the
    Solidification may still remain partially dissolved in the matrix. Higher levels of Al can reduce the density of the melt and thus increase the density difference to the hard particles. An Al content of up to 3% in the matrix is possible. 25
    The base compositions for the matrix are in particular the alloys of alloyed tool steels, as described in the standard DIN 10020. Both cold work tool steels, hot work tool steels and high speed steels can be used as the base composition for the matrix. In order to avoid eutectic carbides it is sometimes necessary to reduce the carbon content of the high-speed steels compared to the standard composition. With these matrix alloys it is possible, by a suitable heat treatment, which generally consists of a hardening process and a hardening process, and a · · · · · · · · ·: ·: · · · · · · · · ··· · ·. , φ, φ · · · ·············································
    Starting process, the required for a trouble-free use of the cutting rings hardness of at least 44HRG can be achieved. It has been found that a particularly good wear resistance is achieved if the matrix of the cutting rings has a hardness of 50HRC and above. This hardness is needed when drilling in hard, very abrasive rock formations. The heat treatment of the cutting rings must always be adapted to the particular application of the application in order to achieve a balance between hardness and toughness of the structure. If the matrix composition is selected according to a manganese-hard steel, the advantage of a particularly tough and impact-resistant basic structure together with a pressure-hardening and therefore wear-resistant surface can be utilized. In "Houdremont, Handbuch der Sonderstahlkunde, Springer Verlag, 1956" and other literatures, manganese hard steels of this type, which are also called Hadfield steels according to their inventor and whose structure is austenitic manganese tool steels, are described. These steels have a manganese content of about 8 wt% to 15 wt%, exceptionally 6 to 25 wt%, and a carbon content of about 0.8 to 2.3 wt%. The ratio of wt% Mn to wt% C is about 10: 1. Manganese hard steels 20 are characterized by a corresponding heat treatment in that their structure consists of a metastable, very tough austenite. By compressing the surface, the metastable austenite can be transformed into a hard and wear-resistant martensite, yielding a hard-surfaced, tough-core component. Depending on the proportion of Mn and C in the steel and their 25 ratio to each other, the conversion behavior can be influenced. For the formation of the hard, martensitic surface alone, the stress during use may be sufficient. If the pressure load during use is insufficient to cause the required transformation of the microstructure in the region of the surface, then the surface area to be hardened can be hardened, for example, by hammering or another mechanical treatment even before use. The composition of the matrix alloy can also be adjusted so that the surface or the entire tool body can be cooled by cooling below room temperature, preferably by means of liquid 8 9/25 ····· ··· • • • • • • • • • • • • • • • • • • • • • • · · · · ·
    Nitrogen, at least partially converted into martensite.
    There may be described above roller bits or similar annular tools, which contain at least one radially outwardly directed working area 5 and an axially closer clamping part, and of an iron-based alloy as a matrix, in which hard material particles, such as carbides and / or nitrides and / or
    Carbonitrides and / or borides, optionally embedded in a mixed form of the elements of Groups 4 and / or 5 of the Periodic Table, are made in which in a first step, a base alloy, for example in an induction furnace, melted and to a temperature of 1350 ° C is heated to 1630 ° C. This base melt is used to bring most of the alloying elements for the subsequent finished alloy in the melt.
    Depending on the desired matrix composition, and depending on the desired matrix composition, the base melt may have the following composition in% by weight: 15
    Carbon (C) to 2.5 Silicon (Si) 0.01 to 3.0 Manganese (Mn) 0.05 to 28.C Chromium (Cr) to 9.0 20 Nickel (Ni) to 4.3 kiA QC WiOiyDQan ^ MO / Tungsten (W) DIS to 2.2 (1.5 xMo + W) to 5.1 vanadium (V) to 6.0 25 niobium (Nb) to 35.0 aluminum (AI) optionally to 3.5 titanium (Ti) to 2.0 zirconium (Zr) to 3.0 30 hafnium (Hf) to 1.0 tantalum (Ta) to 5.0 Cobalt (Co) to 3.5
    Iron (Fe) and impurity elements as remainder. 9 10/25 • • • • • • • • • • • • • * * ···· • • • • •: • «• • • • • • • • • • • • • • • • • • • • • * • • • e * *. • • • • • • • • • • · ·
    If the metallic constituents of the hard material particles to be formed later are already contained in the base melt (elements from groups 4 and 5) and at the same time the proportion of C, N and B is kept as low as possible, then in a second step carbon and / or nitrogen become and / or boron are introduced into the base melt, whereupon these elements combine with the elements of group 4 and / or 5 of the periodic table which are already in the base melt to form hard material particles which have a higher density than the melt. The hard materials formed have the structure Mx (C + N + B) y, wherein the sum of components io of carbon, nitrogen and boron in the hard materials formed between 0.4 and 0.55 atomic components, or the ratio x: y is between 1.5 and 0.8. The amount of alloyed carbon is to be selected such that in the residual melt a Köhlenstoffgehalt of 0.3 to 2.3 wt% C remains. Thus, sufficient carbon is available for the formation of 15 martensite in the matrix during the subsequent heat treatment. The amount of the other alloying elements, except those of the 4th and 5th group, depends on the desired properties of the matrix surrounding the hardening particles, whereby the formation of a eutectic carbide network to achieve the highest possible toughness should be avoided. Particular attention should be paid here to the 2o heat treatment properties of the matrix.
    A rapid formation of hard materials with low wear of the melting vessel is obtained when the temperature of the base melt is maintained between 1550 ° C and 1630 ° C. The alloying of carbon, nitrogen and boron can be achieved by solids such as coke, high-ferrochrome
    Carbon content, silicon carbide, Ferrostickstoff and Ferrobor or by adding carbon and / or nitrogen and / or boron-containing melts or gases. This component or components may or may also contain other alloying elements. Depending on the carbon, nitrogen and boron content of the added comonomers or components, very large amounts of these may be necessary to achieve the desired carbon, nitrogen and boron levels in the final melt. The amount of added carbon, nitrogen and boron carriers can thus be significantly greater than the amount of 10 11/25 ·· «· ···· ·· ···· · ·« ·: ·: · · · ······················································································
    Base melt, whereby the alloying element portions in the base melt can assume very high contents, e.g. Niobium up to 35% by weight,
    The melting of an alloy comprising elements of the 4th and / or 5th main group with low contents of carbon, nitrogen and boron has the advantage that the ferroalloys, over which the elements of the 4th and 5th groups are generally alloyed will dissolve quickly. If the contents of carbon, nitrogen and boron in the melt are too high, a layer of hard material can form on the surface of the ferro alloy pieces used, which severely hampers the dissolution. It has been shown in tests that the proportion of io carbon in the base melt in the above case should be less than 0.6 wt .-%.
    It is also possible to adjust the composition of the Bäsisschmelze in the first step so that it does not contain the elements for forming the hard particles and in the second step, the hard material particles, by means of a solid or liquid, metallic pre-melt or by means of a similar mixture of metal and Hard material particles, added and homogeneously distributed in the base melt. These hard particles may be carbides and / or nitrides and / or oxycarbonitrides and / or borides, optionally as carbonitrides and / or oxycarbonitrides with borane moieties, at least one of the elements or in mixed form 20 of the elements of groups 4 and 5 of the periodic table. The homogeneous distribution of the hard material particles in the base melt can be assisted by mechanical processes, for example by stirring, or also by the injection of gases in the lower region of the melting vessel. Depending on the composition of the composition of the formed or introduced hard material particles, it may be advantageous, for example, to prevent oxidation of constituents in the melt, the process steps 1 and / or 2 in the whole or even partially under a protective gas atmosphere or under reduced ambient pressure perform.
    After the homogeneous distribution of the hard material particles in the second step, the matrix melt with the hard material particles contained therein is poured in a third step into a rotating mold and allowed to solidify. Called 11 12/25 30 ·· * · ···· · «······················································································· By the rotational movement about the longitudinal axis of the mold and the thereby acting on the melt and the hard particles centrifugal force, the hard particles migrate outward into the later work area of the roller chisel, where they form a very rich in hard materials microstructure. At the same time, a microstructure forms in the interior, which has only small contents of the primary precipitated or introduced hard materials. The resulting proportion of exterior hard materials is determined predominantly by the process parameters of the speed of the mold, the density difference between the hard material particles and the melt, the size distribution of the hard material particles and the cooling rate of the melt in the rotating mold. In order to achieve a high concentration of hard material particles in the outer region and thus a high wear resistance, the speed of the mold and thus the force acting on the melt and on the hard particles centrifugal acceleration should be as high as possible. Centrifugal accelerations of 700 m / s 2 and above, measured on the outside diameter of the casting, have been proven. A high density difference between the hard material particles and the melt can be achieved above all by high proportions of niobium, tantalum and hafnium in the hard materials. For cost reasons, niobium-rich hard materials, in particular niobium-vanadium mixed carbides, have proven to be favorable for achieving a high proportion of hard material. In any case, the hard-substance particles precipitated or added in the second step should have a density which is greater than that of the matrix melt at a temperature of 50 ° C. above its liquidus temperature.
    The migration of the hard particles to the outside requires different feit depending on the size of the casting and to achieve a maximum possible concentration of hard materials in the outer structure, the time between the Eingusszeitpunlct the enamel into the mold and the solidification of the melt should be as large as possible. Preheating the mold to several 100 ° C can bring slight benefits here. The speed of solidification can be particularly reduced if the mold as a whole or in parts facing the casting is made of a material which conducts the heat very poorly. Here are mainly quartz sand and mold materials based on aluminum silicate 12 13/25 ". ». * · * • · · · · ·« · · · · · · · «··· * ··············································
    To call ceramics. A ceramic-based or carbon-based heat-insulating coating on the inside of the mold also brings advantages,
    After the blank has been cast, it can be removed from the mold at a temperature of up to 1000 ° C. in order to keep the stresses in the ring 5 low, the temperature can be equalized over the entire ring in an oven and then cooled down so slowly. the matrix structure is in a soft state at room temperature. The cooling rate depends here on the alloy composition 10 of the matrix. If the later conditions of use of the roller bit require it, e.g. drilling in particularly hard rock, so after emptying the blank from the mold this can be brought in an oven to the appropriate forging temperature and then be plastically deformed in the drop forging process in one or more stages. Through this process, the i5 toughness of the structure can be increased significantly. The forging process then includes the controlled cooling to room temperature. Thereafter, the blank can be mechanically preprocessed by, for example, turning, followed by heat treatment of the ring. This can, in the case of a matrix composition similar to a tool steel, consist of a hardening process 20 and at least one Aniassvorgang. In the case of a matrix composition similar to a manganese-hard steel, rapid cooling generally takes place after an annealing treatment in order to achieve a metastable, austenitic structure. After the heat treatment, the mechanical finishing of the cutting ring is followed by e.g. Turning and / or grinding. 25
    Subsequently, the invention will be described with reference to an example carried out.
    A pre-melt with 0.28% C, 1.3% Si, 0.9% Mn, 1.34% Cr, 2.2% Ni, 0.1% Mo, 0.8% V and 10.0% Nb was melted in an induction furnace, brought to a temperature of 1590 ° C, kept at this temperature for 5 minutes and then brought to a carbon level of 2.35% with petiole coke at the same temperature. After carburizing, the temperature of the final melt 13 14/25 '·· ♦ · ···· ·· ···· ········································ • ······················································································································· : Lowered to 1570 ° C, held there for 3 minutes and then poured off in a centrifugal casting process. As a centrifugal casting mold, a steel mold was used, in which a core of bonded silica was inserted. This core was previously coated on the inside surface with 1mm thick 5 zirconia base size. The casting was removed at about 800 ° C from the mold and after a compensation phase of 60min in the oven in this cooled to room temperature, then preprocessed and brought by hardening and two tempering to a hardness of 53 HRC in the clamping range. 1 shows an example of a cut annular roller chisel 1 with the cross section 2. The enriched with hard particles Part 3 includes lying on the outer diameter of the ring 1 work area 4. The Spahnbereich 5 is located on the inner diameter of the ring 1 and contains only a small proportion of hard materials. Figure 2 shows an example of the structure in the work area 4, wherein the
    Hard material particles are bright and the matrix is shown dark. The hard material content is about 20%.
    For comparison, FIG. 3 shows the microstructure in the clamping region 5 with only a small proportion of hard materials. 14 15/25
    权利要求:
    Claims (12)
    [1]


    • Patent claims i. Ring-shaped tool (1) with at least one radially outwardly directed working area (4) with high wear resistance and an axis closer 5 clamping part (5), the person skilled in the art as a roll chisel for rock or as a cutting ring, in particular for tunnel boring machines, known, characterized in that the Tool consists of a material which is formed from an iron-based alloy as a matrix with embedded hard particles, wherein the hard material particles of carbide and / or nitride and / or oxide and / or boride, optionally as io carbonitride or oxycarbonitride with boron at least one of the elements, or in the mixed form of the elements of Groups 4 and 5 of the Periodic Table, and have a density at room temperature greater than 7400 kg / m3, preferably greater than 7600 kg / m3. i5
    [2]
    2. Tool (1) according to claim 1, characterized in that the hard material particles to an extent of at least 5 vol .-%, in particular of more than 8 vol .-%, are present in the tool, wherein the hard material particles on the Werkzeugquerschnift (2) are distributed inhomogeneous and in the work area (4) have a higher density. 20
    [3]
    3. Tool (1) according to claim 1 or 2, characterized in that the working area (4) has a volume proportion of at least 8.0%, preferably of at least 14.0%, in particular from about 20 to 25%, of the tool (1), in which working area more than 60 vol .-%, preferably more than 75 25 vol .-%, the hard particles are formed with a size of less than 70 pm.
    [4]
    4. Tool (1) according to any one of claims 1 to 3, characterized in that the hard material particles are formed substantially as niobium-vanadium mixed carbides, optionally with a Stickstoffanteii, and a ratio of 30 at .-% Nb to At.- % V of greater than 5, preferably greater than 10, have. Nb fAt .-% 1 V [At .-%] > 5, preferably > 10
    [5]
    5. Tool (1) according to one of the preceding claims, characterized 16 16/25: ····· ······· C) 0.28 to 2.3 silicon (Si) 0.01 to 2.0 5 manganese (Mn) 0.05 to 25.0 chromium (Cr) to 6.0 nickel (Ni) to 2.5 molybdenum (Mo) to 2.2 tungsten (W) to 15 10 (1.5xMo + W) up to 3.5 vanadium (V) to 0.8 niobium (Nb) to 0.4 cobalt aluminum / all to 3.0 to 3 0 15 1III II "4111 · (^ 1 / optionally MIO v, U titanium (Ti) to 0.2 zirconium ( Zr) to 0.2 hafnium (Hf) to 0.1 tantalum (Ta) to 0.25 20 iron (Fe) and impurity elements as balance.
    [6]
    6. Tool (1) according to claim 5, characterized in that the matrix alloy of tool steel having a hardness of greater than 44 HRC, 25, preferably 50 HRC and higher exists.
    [7]
    7. Tool (1) according to claim 5, characterized in that the matrix alloy of manganese steel with a manganese concentration of 6 to 25 wt .-% Mn, preferably from 0 to 15 wt .-% Mn consists. 30
    [8]
    8. Method for producing annular tools (1) with at least one radially outwardly directed working area (4) and an axially closer clamping part (5), known to those skilled in the art as a roller chisel or cutting ring. 17 17/25 ·· ·· ·· ··· '································································································ It is made of an iron-based alloy as a matrix in which hard material particles, such as carbides and / or nitrides and / or carbonitrides and / or borides, optionally in a mixed form of the elements of groups 4 and / or 5 of the periodic table, optionally for the production of a tool according to at least one of the 5 preceding claims, wherein in a first step, a base alloy is melted and heated to a temperature of 1350 ° C to 1630 ° C and in a second step, an addition or formation in or in the melt of the base alloy Hard material particles having a higher density are then carried out, whereupon, in a third step, the matrix melt with the hard material particles in a mold for the annular tool is subjected to a rotational movement about the longitudinal axis and allowed to solidify.
    [9]
    9. The method of claim 8, wherein in the first step, a base alloy having a chemical composition in wt .-% of carbon (C) to 2 * 5 silicon (Si) 0.01 to 3.0 manganese (Mn) 0.05 to 28.0 chromium (Cr) to 9.0 Nickel (Ni) to 4.3 Molybdenum (Mo) to 3.5 Tungsten (W) to 2.2 (1.5xMo + W) to 5.1 Vanadium (V) to 6.0 Niobium (Nb) to 35.0 Aluminum (AI) to 3.5 optionally titanium (Ti) to 2.0 zirconium (Zr) to 3.0 hafnium (Hf) to 1.0 tantalum (Ta) to 5.0 cobalt (Co) to 3.0 iron (Fe) and impurity elements as the remainder is melted. 18 18/25 • • • • * • • • • • • • • • • • • • • • • • • • • • • • • • • • • • • · · · · · · · · · · · · · · · · · · ·
    [10]
    10. The method according to any one of claims 8 or 9, wherein in the second step, the hard material particles, such as carbides and / or nitrides and / or Oxikarbonitride and / or borides, optionally as carbonitrides and / or Oxikarbonitride with borane, at least one of the elements or in Mixed form of the elements of groups 4 and 5 of the periodic table by means of a solid or liquid, metallic pre-melt or by means of a similar mixture of metal and hard particles with a diameter of the hard particles of less than 70 pm introduced into the liquid base alloy and distributed homogeneously in this after which, in the third step, under rotary motion in the mold, a solidification of the mixture of hard material particles and a matrix alloy, formed from the base alloy and the metal portion of the melt, takes place.
    [11]
    11. The method according to any one of claims 8 or 9, wherein the base alloy is melted with i5 a carbon content of less than 0.6 wt .-% C and heated to a temperature of 155Q ° C to 1630 ° C, after which in a second step, an addition of Alloying elements carbon and / or nitrogen and / or boron, optionally as a master alloy, takes place and these elements with the dissolved elements of group 4 and / or group 5 of the periodic table in the primary melt carbide and / or nitrides and / or borides and / or form compounds or mixtures thereof, wherein the forming hard material particles have a sum fraction of carbon, nitrogen and boron of 0.4 to 0.56 atomic components and a higher density than the melt and that 0.3 to 2.3 wt carbon remains in the liquid metal, whereupon in a third step Melt in a mold for the annular tool subjected to a rotational movement about the longitudinal axis and allowed to solidify and, in further steps, a processing and a heat treatment of the tool.
    [12]
    12. The method of claim 11, wherein the elements of Groups 4 and 5 of the Periodic Table are selected in their respective concentration in the base alloy, that the density of the primary precipitated hard material particles is greater than that of the melt at a temperature of 50 ° C above the liquidus , 19 19/25
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    同族专利:
    公开号 | 公开日
    EP2984287A2|2016-02-17|
    WO2014165887A2|2014-10-16|
    WO2014165887A3|2015-02-12|
    CN105339587A|2016-02-17|
    US20160298451A1|2016-10-13|
    DE202014101693U1|2014-05-14|
    AT514133B1|2017-06-15|
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    CN105886947A|2016-04-18|2016-08-24|和县隆盛精密机械有限公司|Abrasion-resistant taper-shank twist drill and preparation method thereof|
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    CN108203791A|2017-12-20|2018-06-26|柳州璞智科技有限公司|A kind of mold materials and preparation method thereof|
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    法律状态:
    2018-12-15| MM01| Lapse because of not paying annual fees|Effective date: 20180412 |
    优先权:
    申请号 | 申请日 | 专利标题
    ATA300/2013A|AT514133B1|2013-04-12|2013-04-12|Ring-shaped tool|ATA300/2013A| AT514133B1|2013-04-12|2013-04-12|Ring-shaped tool|
    EP14723967.7A| EP2984287A2|2013-04-12|2014-04-09|Annular tool|
    US14/782,987| US20160298451A1|2013-04-12|2014-04-09|Annular tool|
    PCT/AT2014/050084| WO2014165887A2|2013-04-12|2014-04-09|Annular tool|
    CN201480021044.0A| CN105339587A|2013-04-12|2014-04-09|Annular tool|
    DE202014101693.7U| DE202014101693U1|2013-04-12|2014-04-10|Ring-shaped tool|
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