EP1812609A1

EP1812609A1 - Method and device for shaping wire-shaped and rod-shaped starting materials close to the gauge block, and correspondingly produced flat profiled element

Info

Publication number: EP1812609A1
Application number: EP05789611A
Authority: EP
Inventors: Hans-Toni Junius; Heinz HÖFINGHOFF; Norbert BRACHTHÄUSER; Victor Blinov; Rudolf Kawalla
Original assignee: CD Waelzholz Brockhaus GmbH
Current assignee: C D Waelzholz GmbH
Priority date: 2004-10-02
Filing date: 2005-09-13
Publication date: 2007-08-01
Anticipated expiration: 2025-09-13
Also published as: DE112005003068A5; BRPI0516301A; EP1812609B1; CA2582731A1; MX2007003830A; DE102004048443B3; US20080006350A1; WO2006050680A1

Abstract

The invention relates to a method for shaping wire-shaped and rod-shaped starting materials (17) by rolling, especially for rolling flat profiled elements (18) consisting of a wire rod. The starting material (17) is heated in a heating station (5) at a desired temperature, shaped during at least one rolling process (7), and then cooled. According to the invention, once the starting material (17) has been heated in the heating station (5), it is cooled in a cooling station (14) to a pre-determinable rolling temperature; it is then shaped into a flat profiled element (18) by rolling close to the gauge block, and then cooled and/or subjected to a subsequent treatment according to joining properties to be correspondingly adjusted. In this way, a series of different methods can be carried out by means of an installation for rolling starting materials with a patented structure, an austenite structure, a bainite structure or an undercooled austenite structure.

Description

Method and device for final measure

Deformation of wire- and bar-shaped primary material as well as correspondingly produced flat profile

description

The present invention relates to a method for near-end deformation of wire and rod-shaped starting material according to the preamble of claim 1, a device suitable for carrying out the method according to claim 26 and to a flat profile produced according to the method according to claim 38.

The production of relatively narrow and flat strips of steel materials, referred to below as flat profiles, can be carried out in various ways, depending on the required material properties, the dimensions of the flat profiles to be produced and the intended use of the flat profiles. Under flat profiles are usually understood profile shapes in which the width of the cross section is not greater than 10-20 times the thickness. Such flat profiles are used for functional components and often wear parts in technical equipment, e.g. used for springs or the like. Components in the automotive, aircraft and space industry, in equipment construction and agricultural machinery. Also, such flat profiles are used as starting material e.g. used for the production of saws, saw blades, bushing chains for motorcycles and bicycles, rollers, rolling bearings, ski edges or also for piston rings. Often, these flat profiles are mechanically highly loaded components, whose strength properties are of key importance in addition to compliance with required cross-sectional shapes and dimensions.

With properties usually required, such flat profiles are often cut out of wider steel strips by longitudinal division, whereby commercially available steel strips can be used as starting material, which can be brought to the corresponding dimensions by known hot and / or cold rolling processes. The setting of the material properties is usually unproblematic in such steel bands, but changes in the longitudinal division of the material of the flat profiles no longer compared to dem¬ those of steel strips. However, flat profiles produced in this way have the disadvantage that certain designs of the edges of the flat profiles required or advantageous due to the later uses of the flat profiles are not exhibited, which certainly have important advantages for the serviceability or service life of components produced therefrom. Thus, after the longitudinal division of steel strips from wide steel strips, edge formation must be worked on by additional machining processes after longitudinal slitting, resulting in additional costs.

Another possibility for producing such flat profiles consists of drawing the materials as wire by means of correspondingly shaped drawing dies which automatically produce the required profile cross-sections and their fine geometry as well as the edge configuration. The problem with the pulling of corresponding flat profiles which is otherwise widely used for wire production is the relatively low attainable pull speeds due to the otherwise excessively high wear of the drawing molds and also the strain hardening of the materials due to the forming, which occurs only when the corresponding materials are drawn consuming intermediate heat treatments of the drawn wires can be undone. As a result, such a production of flat profiles is complicated and technically not without problems.

It is also known to produce corresponding flat profiles by cold rolling, by a relatively small cross-sectional decreases, for example, as a round wire ausge¬ led starting material gradually and depending on the respective deforma tion by cold rolling in a flat profile is formed. In this case, it is also possible to ensure the dimensions and the required edge shapes by appropriate technology management. The disadvantage here, however, as in all cold rolling, that the cold-rolled materials similar to pulling a corresponding strain hardening subject and therefore must be treated in the same way analogous to the necessary heat treatment during drawing. However, in the case of strong cross-sectional changes, this necessitates frequent intermediate annealing of the materials in the course of cold rolling. It is therefore an approach for further developing the rolling of flat profiles made of wire-like starting material has become known in which instead of cold rolling a hot rolling is carried out according to EP 0 314 667 B2 to the substantial change in cross section during the forming of the wire-like starting material in much easier deformable warm state to carry out the material. For this purpose, the wire-like starting material is heated by conductive heating to a temperature of at most Ai or the transition temperature in the γ-region of the alloy and then rolled in a multiple stand. Subsequently, the rolled flat profile can then be cooled. A disadvantage of this procedure is that although the forming process can be carried out with relative final dimensions, the control of the material properties of the material in such process control is anything but simple. Also, the processing of steel materials is limited only to certain classes of materials.

The object of the present invention is therefore to provide a method for near net deformation of wire and rod-shaped starting material, which combines the advantages of thermoforming of wire and rod-shaped starting material with compliance with the process parameters relevant to the material characteristics process, thereby producing a variety of different, but nevertheless allows very consistent ein¬ adjustable material and workpieces properties.

The solution of the object according to the invention results from the characterizing features of claim 1 with regard to the method for continuous running of strip steel, with regard to the method suitable for carrying out the method from the characterizing features of claim 26 and with regard to a flat profile produced in this way from the characterizing features of Claim 38 each in cooperation with the features of the associated preamble. Further advantageous embodiments of the invention will become apparent from the dependent claims.

The invention according to claim 1 is based on a process for the rolling technical deformation of wire and rod-shaped starting material, in particular for rolling flat profiles made of wire rod, in which the heating of the starting material takes place in a heating station to a desired temperature, the starting material in - A -

deformed at least one rolling operation and then cooled. A der¬ like generic method is further developed in that after the heating of the starting material in the heating station, the starting material cooled in a Kühlsta¬ tion to a rolling temperature, at this rolling temperature near-net-formed into a flat profile and then cooled according einzustel¬ lender structural properties and / or after-treatment. Due to the targeted cooling of the material to the desired rolling temperature before the rolling process is carried out, in spite of the previous heating of the material to a required to trigger the desired microstructural transformations, usually higher temperature can be achieved that exactly before rolling the starting material the initial structure can be adjusted, which, together with the change in the material due to the rolling and a subsequent treatment of the flat profile which may be subsequently adjusted to the rolling, ensures the desired structural properties of the flat profile. Hereby, by heating the starting material to e.g. a temperature which ensures a safe Austenitiserung above the As temperature, ensures a corresponding microstructure conversion, which then sets by the targeted cooling of the starting material to the rolling benö¬ required temperature a structural state, which essentially the Ausgangs¬ base for changing the Structure of the flat profile towards the finished, close to the final cross-section allowed. Here, further aftertreatments such as cooling and tempering may follow, which allow a further change in the structural properties. Thus, a possibility has been found to combine end-to-dimensional deformation of flat profiles produced from steel materials in the hot state with a targeted microstructure adjustment with regard to material properties to be set, which minimizes the after-treatment of flat profiles produced in this way.

It is particularly advantageous if the heating of the primary material in the heating station is at a temperature above the A ₃ temperature of the γ mixed crystal (austenite). In this way, an extremely different microstructure can be produced from an austenitized microstructure as initial structure prior to the rolling of the primary material, which structures can be used to produce the various materials required for the typical applications of the flat profiles. correspond to properties of the steel material and thus enable a wide field of application according to manufactured Flachprofiie.

Another embodiment of the method according to the invention provides that the heating of the starting material in the heating station to a temperature in the region of the α / γ mixed crystal (ferrite / austenite) takes place. As a result, an advantageous starting structure for the subsequent rolling can be set in a targeted manner, in particular for steels with low carbon content.

It is also conceivable in another embodiment that the heating of the Vor¬ material in the heating station to a temperature close to the A-i point. In this way, other processes of structural transformation during the rolling of the starting material can be triggered again, which leads to a further spectrum of structural formation of the rolled and possibly post-treated flat profile.

It is of considerable advantage for carrying out the method if round wire or oval wire is used as the preliminary material. By round wire is meant in this context not only wire with a circular cross-section, e.g. can be made by rolling or drawing technology, but generally wire any cross-section, which is suitable for deformation by rolling technical means towards a flat profile. Corresponding Ovaldrähte here have an oval cross-section. In this case, the free expansion of the round wire or oval wire is generally utilized in a rolling process in order to cause on the one hand demanded property changes with regard to the geometry of the flat profile and on the other hand to produce the required microstructural properties and thus the material properties of the finished flat profile. Such round wire or oval wire is a commercially available starting material and can be obtained commercially in a variety of compositions and alloys, whereby the costs for such round wire or oval wire are relatively low.

It is conceivable here that the round wire or oval wire runs through the process as a windable prematerial. As a result, a quasi-continuous processing of the round wire or oval wire usually supplied on rings is possible, which can also be further processed as a wound-up coil of the finished flat profile as a windable finishing material. It is in another form But also conceivable that the round wire or oval wire as rod-like Vor¬ material passes through the process, the bar-like starting material accordingly also rod-like flat profiles results.

It is advantageous if unalloyed or low-alloyed carbon steels are used as the starting material. Such unalloyed or low-alloyed carbon steels form the starting material for the production of many different components and components and offer a wide range of application areas for the use of flat profiles produced according to the invention.

It is conceivable here that the heating of the starting material takes place in the heating station to a temperature above the A ₃ point. Such a temperature of the starting material is clearly in the range of austenite for the steels usually used in this case, so that the austenitizing processes occurring in the structure form the basis for a number of customary changes in the material properties with regard to the material properties of the flat profiles to be achieved.

A first embodiment of the method according to the invention can be seen therein, when the cooling in the cooling station cools the starting material before rolling to a temperature for setting an austenite microstructure only slightly above the A ₃ temperature of about 800 ^° C. As a result, the rolling process itself is still carried out in the form of the austenite of the microstructure of the starting material as austenitic structure, whereby correspondingly simple diffusion processes can take place and the influencing of the intended microstructural changes can be carried out in a controlled manner.

For this purpose, in a further advantageous refinement of this embodiment of the method, after the flat profile has been rolled in the temperature range of the austenite structure, cooling of the austenite structure for conversion into a sorbitol structure is then carried out directly afterwards. This sorbitol structure has a very fine lamellar structure and offers the best conditions for certain areas of application of such flat profiles.

Another embodiment of the method according to the invention can be seen therein, when the cooling in the cooling station, the starting material before rolling a temperature for setting a Patentiergefüges, eg for a steel C75 between 400-550 ⁰ C cools. Such a Patentiergefüge is formed from a fine-grained pearlite and is particularly well, for example, for further cold drawing ent speaking flat profiles or for applications of flat profiles, where high tensile strengths must be combined with good toughness of the materials. A correspondingly slow cooling of the patenting structure from the pearlite stage usually follows the rolling process. The formation of a patented joint (the same applies to the bainitic structure and austenite microstructure below) takes place for each material relevant here because of its composition at a different temperature, but this is known and characteristic for each material. The relationships between the microstructure conditions and the respective temperatures and process guides of the different materials can be read off from so-called time-temperature conversion diagrams (so-called ZTU diagrams). Therefore, below the temperature for setting a Patentiergefüges (respectively a Bainitgefüges or Austeritgefüges) although for each relevant material different, but with specification of a corresponding material but unique temperature understood, for purely as an example of a steel C75 also specific values are given. Otherwise, the person skilled in the art knows for each material relevant here which temperatures he must set for setting a patenting structure or a bainitic structure or an austenitic structure.

A further embodiment of the method according to the invention can be seen therein when the cooling in the cooling station cools the starting material before rolling to a temperature for setting a bainite structure, eg for a steel C75 between 275-37O ⁰ C. Here, the starting material is still cooled in contrast to the setting of a Patentiergefüges until the rolling of the starting material is carried out in a structural state of the intermediate bainite in which due to the low temperature diffusion processes are largely prevented and by folding over austenite in the material α- grid areas form. This is then precipitated by fine-grained cementite with the advantageous effects for the microstructural properties. An alternative embodiment of the method according to the invention can be seen ge, when the cooling in the cooling station, the starting material before rolling zen to a temperature for setting a supercooled austenite, eg for a steel C75 between 220-280 ⁰ C cools. By correspondingly rapid cooling of the structure from the austenite, otherwise running conversion processes are delayed or can not occur at all or not at all, so that the rolling of such a rapidly cooled, undercooled austenite structure offers the possibility of largely or exclusively converting to make a martensite with the known needle-like hardened structure, which accordingly high-strength materials are produced, with which in further Ausges¬ eg directly followed by a tempering treatment can be carried out with a cooling of the flat profile before winding. By tempering treatment, the material is changed once again in terms of hardness and toughness and thus achieves high hardness with nevertheless good mechanical strength properties.

However, it is conceivable in a rolling of the starting material as undercooled austenite, that after rolling the flat profile directly followed by a tempering treatment without quenching the supercooled Austenitgefüges, but with a Anlaßbehand¬ possibly to form a Bainitgefüges and a tempering treatment with a cooling of the flat profile before winding is carried out. In this case, instead of the martensite formation described above, the intermediate-structure bainite is produced, which has the properties already advantageous above.

Furthermore, it would also be conceivable without generation of supercooled austenite directly to roll as has been described above in ^'the austenite phase, after Wal¬ zen of the flat profile in Tempera door area of the austenite dung to Martensitbil¬ deter, but directly followed by a tempering treatment, and a Ab¬ cooling of the flat profile before winding up. Hereby a ange¬ let martensite structure is produced, which also has the advantages already mentioned. An advantage of all these different process guides is when the starting material is held during the rolling process at least on the set after cooling of the starting material in the cooling station temperature. As a result, the structure does not change during rolling or not too strong, so that the rolling alone causes no structural changes. Depending on the design of the rolling process, heat may have to be removed from the rolling zone with regard to the forming work introduced into the starting material and the resulting temperature change of the starting material, for example at high degrees of deformation or, for example, at low deformations of the starting material For example, by tempering the rollers at the desired temperature by Wärmezu¬ be kept.

Furthermore, it is conceivable that, depending on the choice of process procedure to be carried out, the starting material, after the forming by means of rolling, is subjected to the end-dimensional flat profile of further cooling, in particular rapid cooling. For this purpose, the material which is already present as a flat profile may be e.g. a water cooling or the like. Well-known cooling methods are subjected.

It may also be useful if the rapid cooling cools the rolled flat profile at least below the temperature limit for the course of oxidation processes on the surface of the flat profile and thus ensures that Verzond- rungsvorgänge or the like. No more or no longer can proceed to an improper extent.

It is advantageous if the cooling of the starting material takes place after passing through the heating station and before rolling in a tempered metal bath. Derarti¬ ge tempered metal baths are basically known and tested and offer the ability to target and accurately tempering continuous metal bands and also to keep at a predetermined temperature to run appropriate Aus¬ equal operations without the surfaces of the metal bands of unacceptable oxidation get abandoned.

Here, in a further embodiment, it can also be considered that the material for cooling the pre-material after passing through the heating station remains in the temperature-controlled metal bath for a predeterminable time, in particular the temperature. Run through metal bath a predetermined time to run the already mentioned compensating processes for controlling the temperature of the entire cross section of the starting material.

It is furthermore advantageous if the heating of the primary material takes place by means of inductive heating and / or conductive heating and / or by means of liquid metal baths. Of course, other Aufhei¬ tion methods not discussed here are conceivable, which are known and customary in metallurgy.

An improvement in the surface of the flat profile can be achieved if the heating of the starting material is carried out under inert gas. As a result, oxidation processes occurring during the heating of the primary material are prevented, which of course then do not propagate through the entire process control and thus can not cause any later dimensional deviations or surface defects.

It is also conceivable that a comparison device for temperature compensation within the heated starting material is passed through between the heating station and the cooling station, wherein in a further embodiment the comparison of the temperature within the heated starting material is carried out after passing through the heating station under protective gas influence can be.

The invention further relates to a device for carrying out a method according to claim 1, in which the device in the direction of passage of the starting material, a winding / withdrawal device for unwinding the aufwi¬ ckelbaren starting material or a feed device for the rod-shaped Vormate¬ Rial, a heating station, a cooling station for setting a rolling temperature, a rolling station, a cooling section and a winding / withdrawal device for winding the windable flat profile or a discharge device for the rod-shaped flat profile. This basic configuration of the device makes it possible to carry out the basic process variants in which, after heating, a targeted cooling of the starting material to a temperature is carried out, which comprises rolling the starting material with a structure either as an austenitic structure, as a patented structure, as a bainite structure or as a supercooled austenite allows. Here, depending on the gradient of the cooling and the cooling time, the corresponding Microstructure can be adjusted. Further aftertreatments or intermediate operations can be carried out by interposing or connecting additional accessory device components such as, for example, heat treatment processes such as tempering or tempering processes such as holding the starting material at a specific temperature over a defined period of time To be able to run off compensation processes within the material.

It is advantageous if the rolling station has at least one rolling device, preferably several rolling devices connected in series. As a result, careful shaping of the starting material during rolling can be achieved by targeted design and even sequential arrangement of several rolling devices.

It is also conceivable that in the region of the at least one rolling device, a temperature monitoring for detecting the temperature of the starting material before / and / or after rolling is arranged, with the e.g. with respect to the microstructure, detected impermissible temperature changes during rolling, and e.g. can be turned off zen by tempering the Wal¬ by targeted heat input into the rollers.

For the targeted heating of the starting material, it is advantageous if, for the heating of the starting material by means of conductive heating current-carrying contact rollers are arranged in the inlet region of the device for the starting material. Such conductive heating of the primary material, which is known in principle, permits well controllable heating and thus structural transformation of the primary material.

A particularly favorable cooling of the starting material can be realized if the cooling station has a tempered metal bath to set a rolling temperature. Such a tempered, such as a metal bath of a lead-bismuth alloy, is already widely used and is therefore known and tested in terms of its behavior. However, even with relatively longer throughput times of the starting material by means of such a metal bath, it is possible to ensure reliable tempering of the starting material while at the same time preventing oxidation processes on the surface of the starting material. It is conceivable here that the tempered metal bath is arranged before and / or after the rolling station. Depending on the procedure, the heating temperature in the heating station can be rolled out directly from the austenite phase, with appropriate tuning of the heating temperature, so that the metal bath can then be tempered

5 flat profile for the formation of bainitic interstitial structure takes over. In other cases, the metal bath is used for targeted cooling of the starting material to the rolling temperature and must of course then be placed in front of the rolling station. In this case, in a further embodiment, the temperature-controlled metal bath can have a wiper and / or deflection device, via which the starting material is guided in the tempered metal bath during the dwell time. The winding or Umlenkein¬ direction can also take over buffer function for downstream device stations.

For certain variants of the process control, it is advantageous if water cooling cools the flat profile with a high temperature gradient in the cooling path. As a result, microstructures achieved after rolling are virtually frozen by the rapid cooling and are retained even at lower temperatures.

In the context of the aftertreatment of rolled flat profiles, it is advantageous if a further conductive heating station is provided for heating the flat profile for post-rolling annealing, in which e.g. the heating can take place again under inert gas influence. It is also possible, for example, to provide a further cooling section for cooling the flat profile within the scope of a tempering subsequent to rolling.

The invention further beschreiebt according to claim 38, a flat profile, produced 5 by the method according to claim 1. Such a flat profile advantageously has a substantially rectangular cross-section or a rectangular cross-section, a variety of configurations of the edge region can be adjusted depending on the subsequent use of the flat profile.

It is advantageous if typical carbon steels, in particular o carbon steels having a carbon content of between 0.10 and 1.35%, in particular also C 10 to Ck 101/125 Cr1, are processable as starting material. Such flat profiles are preferably in dimensions between a thickness of 0.5 - 5 mm and a width of 4 - 25 mm processable.

A particularly preferred embodiment of the device according to the invention for carrying out the method according to claim 1 is shown in the drawing.

Show it:

1 shows a schematic representation of the basic structure of a device for carrying out a method for hot rolling of rolled wires with the most important device components,

FIG. 2 shows a continuous time-temperature conversion diagram for carrying out the method according to FIG. 1,

3 shows a schematic representation of the basic structure of a device according to claim 26 for carrying out the method according to the invention with a cooling of the starting material before rolling for the production of patented structure, bainite structure or a supercooled austenite structure, FIG.

FIG. 4 shows an isothermal time-temperature conversion diagram for carrying out the method according to FIG. 3 with the indication of the respective process control for the production of patented structure, bainite structure or a supercooled austenite structure,

FIG. 5 shows a modified device according to FIG. 3 for the heat treatment of a supercooled austenite microstructure after rolling;

FIG. 6 shows a modified device according to FIG. 3 for the post-rolling heat treatment of an austenitic structure without a cooling device before rolling,

FIG. 7 shows a modified device according to FIG. 3 with a cooling device in front of the rolling station and devices for heat treatment carried out after rolling, FIG. 6 shows a modified device according to FIG. 7 with a cooling device downstream of the rolling station and devices for heat treatment carried out after rolling.

FIG. 1 shows, in a very schematic representation, the structure of a device for carrying out a method for hot rolling of wire rod into flat sections. This is a device for carrying out a process without special means for cooling the starting material before rolling.

A flat profile 18 is to be understood as meaning steel material whose width corresponds to a maximum of 10 to 20 times its thickness and which usually serves as a constructive basis for mainly mechanically loaded components such as springs, piston rings or the like as well as saw blades or other highly stressed components Workpieces use. The dimensions of such flat profiles, in contrast to otherwise produced rolled strip rather low and is typically 5 in the range of up to 30 millimeters in width and 5 millimeters in thickness. The starting material 17 is usually supplied as a round wire rod of the system 1, but may of course have other cross sections as a starting material for rolling in a rolling device 7.

The pre-material 17 is conveyed in Appendix 1 by a reel with a coil outlet 2 o via a caterpillar take-off 3 and a straightening device 4 in a device 5 for conductive heating of the starting material 17, wherein the conductive Ein¬ direction 5 current-carrying contact rollers 16 which over the Coupling of the current in the starting material 17 along the conductive device 5 cause an Er¬ heating of the starting material 17. This heating takes place predominantly in a protective gas channel 6, which prevents the formation of oxidation products on the surface of the primary material 17 during the heating. Subsequent to the second pair of contact rollers 16, a duct-like duct 12, which may also be flooded with protective gas, is provided as a compensation zone, within which the prematerial 17 uniformly heats up in the interior area by means of balancing processes and thus prevents it from entering the rolling device 7 has set a uniform temperature curve within the preliminary material 17. Within this compensation In the zone 12, the temperature of the starting material 17 drops from the final temperature of, for example, during the heat treatment between the contact rollers 16. B. 1020 ° Celsius to a lower temperature, so that within the compensation zone 12, a cooling of the starting material 17 to a temperature eg just above the Aß temperature occurs. With this temperature, which is monitored, for example, before or after the rolling device 7 by a temperature measurement 8 implemented by means of a radiation pyrometer, the starting material 17 enters the rolling device 7 and is shown there in one or more passes (simplified is only one roll ¬ device 7, but it can also be several such rolling devices 7 are connected in series) rolled to the flat profile 18, which then cooled by means of a cooling section 9 with here, for example, two blast chillers 10 and via a Rau¬ penabzug 3 a reel 11 and abandoned there is wound into a coil. The starting material 17 thus passes through the installation 1 in the direction of passage 19 and is supplied to the installation 1 as a wound coil, for example a round wire rod, and wound up as a coil of a flat profile 18.

Such a rolling line 1 carries out a method that according to the figure 2 in a representation in a continuous time-temperature conversion diagram for a steel C 75 illustrated for the production of bainite according to the Temperatur¬ leadership along the line 13 runs. Here, the starting material 17 is rolled at a temperature of just below 800 ° C and then cooled along the line 13. The resulting sorbitol structure provides the corresponding properties of the flat profile 18 produced in this way. A disadvantage of this method is that the temperature of the preliminary material 17 can be controlled relatively costly by cooling only in the compensation zone 12; in addition, the temperature can be controlled Do not reduce to values that would be useful for other procedures.

It is therefore an advancement of the indicated in Figure 1 Appendix 1 inso¬ suggested that according to Figure 3, the system 1 is modified so that before the rolling device 7, a cooling device 14 z. B. consisting of a Metall-, such as a lead-bismuth metal bath, is preceded, in which a targeted cooling of the starting material 17 vor¬ before entering the rolling device 7 is taken so that the structure of the starting material 17 upon entering the rolling means 7 corresponds exactly defined conditions and therefore the deformation of the starting material 17 to the flat profile 18, optionally in conjunction with subsequent treatment operations described further below, the desired structure of the flat profile 18 and the required cross-sectional dimensions and cross-sectional shapes 5 results. Otherwise, the system 1 of Figure 3 essentially corresponds to the Appendix 1 of Figure 1, so that will be discussed in more detail only on the existing differences.

The heating in the conductive device 5 can be carried out in two or more stages, with a number of contact rollers 16 are arranged one behind the other, so o that the heating multi-stage, possibly even using unterschiede¬ ner currents and thus different temperature gradients in the Erwär¬ determination made can be. This usually causes a much better controllable heating of the starting material 17, moreover, 5 already occur during the passage through the conductive device 5 Ausgleichsvor- 5 courses, so that the starting material 17 at the end of the passage through the kondukti¬ ve device 5 very evenly present at about the indicated temperature of 1020 ° Celsius.

The metal bath 14 has for the passage of the starting material 17 a Wickelvorrich¬ device 15 in the form of rolls of z. B. a meter diameter, on the o Vormaterial 17 is wrapped several times and thus remains within a predetermined time within the metal bath 14 while passing through the metal bath 14. The metal bath 14 is tempered in such a way that the desired starting temperature for the rolling of the primary material 17 in the rolling device 7 is set within the material 17 and thus precisely within the primary material 17 the structure can form Rolling is required within the rolling device 7 for achieving the subsequent final structure. In order to prevent impermissible surface changes of the starting material 17 after exiting the conductive device 5 and passing through the metal bath 14, also protective gas channels 6 are arranged before and after the metal bath, so that the starting material 17 is almost completely heated and tempered under a protective gas atmosphere becomes. After rolling in the rolling device 7, the flat profile 18 is cooled by a water cooler or the like via a high-speed cooler 10 and wound up as already described for FIG.

FIG. 4 shows various conceivable processes along the line 13 ^' , 13 ", 13 ^'" in an isothermal time-temperature conversion diagram for a steel C 75, which shows the different final structures of the flat profile 18 to be set after rolling in the rolling device 7 specify. If, for example, the temperature of the primary material within the cooling device 14 is reduced to about 500 ° C. and then rolled, then a so-called patenting structure can be set for this steel according to line 13 ^' , which results in a particularly high toughness high tensile strength values possible. If, on the other hand, cooling is continued in the cooling device 14 to values of approximately 350 ° C., a so-called interstep structure in the form of a bainite structure according to line 13 ^" results during rolling, and a particularly interesting option for producing flat profiles 18 is cooling in the cooling device 14 to be carried out so fast that according to the line 13 ^'" comes in the range below 300 degrees Celsius of the supercooled austenite for rolling in the rolling device 7 and then can perform a martensite hardening of this supercooled Austenites by appropriate treatment.

Thus, by the involvement of a cooling device 14 before rolling in the rolling device 7, the possibility is created to process on a system 1 a very unter¬ different type of materials to flat sections 18 and thereby each optimal process control according to the lines 13 ^' , 13 ^" , 13 ^'" in the figure 4 fah¬ ren.

A modification of the system described in FIG. 3 for the rolling of undercooled austenite as the structure of the starting material 18 is shown in FIG. 5, in which, as far as rolling in the rolling device 7, what was stated for FIG. 3 applies as above. After the rapid cooling 10 after rolling in the rolling device 7, a further conductive device 5 ^'is arranged, which serves to re-heat the flat profile 18 for a compensation of the microstructure of the flat profile 18, likewise being heated conductively again and in a subsequent Quick cooling 10 cooled becomes. This makes it possible to achieve a broad control of the properties of the precursor material 17 rolled as a supercooled austenite.

FIG. 6 shows a further modification of the system 1 in which, according to line 3 in FIG. 4, rolling takes place without a separate cooling device and only after a certain cooling in the compensation zone 12 and thus rolling in the rolling device 7 in the austenite region of the structure of the starting material 17 ausge¬ leads. This Flach¬ profile 18 thus rolled and cooled in the cooling device 10 is then tempered by Vergüteope¬ rations in a conductive device 5 ^' as described above for Figure 5 and thus changed once again in its properties.

According to FIGS. 7 and 8, two variants of the system 1 according to FIG. 5 are shown once again, in which the cooling device 14 is arranged once before and once after the roller device 7, so that the temperature control of the material 17 in the area of the roller device 7 specifically, for example, after Wai- zen in the rolling device 7 by tempering the resulting flat profile 18 can be further changed. The cooling device 14 according to FIG. 8 can serve, for example, for correspondingly slow or targeted tempering of the flat profile 18 after rolling in order to supply the structure of the flat profile 18 after rolling to a targeted change, without directly performing too rapid cooling of the flat profile 18.

Part number list

1 rolling line / plant

2 coil drain

3 caterpillar take-off 4 straightening device

5, 5 ^' - conductive heating

6 protective gas channel

7 rolling device

8 Temperature measurement 9 Cooling section

10 water cooling

11 coiler

12 equalization zone

13-13 ^' "- Temperature control for process variants 14 Cooling station / metal bath

15 winding device

16 contact rolls

17 starting material

18 Flat profile 19 Continuous feedstock

Claims

claims

1. A method for rolling technical deformation of wire and rod Vor¬ material (17), in particular for rolling flat profiles (18) of wire rod, wherein in a heating station (5), the heating of the starting material (17) to a ne desired temperature takes place, the starting material (17) in at least one

Rolling process (7) deformed and then cooled,

characterized in that

after heating of the starting material (17) in the heating station (5) the Vor¬ material (17) cooled in a cooling station (14) to a predeterminable rolling temperature, at this rolling temperature endmaßnah by rolling in a flat profile

(18) deformed and then cooled and / or post-treated in accordance with the structure properties to be adjusted.

2. The method according to claim 1, characterized in that the heating of the starting material (17) in the heating station (5) to a temperature above the Aß temperature of the γ-mixed crystal (austenite).

3. The method according to claim 1, characterized in that the heating of the starting material (17) in the heating station (5) to a temperature in the region of the α / γ mixed crystal (ferrite / austenite).

4. The method according to claim 1, characterized in that the heating of the starting material (17) takes place in the heating station (5) to a temperature in the range close to the ArPunkt.

5. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that is used as the starting material (17) round wire or oval wire.

6. The method according to claim 5, characterized in that the round wire or oval wire as windable starting material (17) passes through the process.

7. The method according to claim 5, characterized in that the round wire a or Ovaldraht Is rod-like starting material (17) passes through the process.

8. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that are used as the starting material (17) unalloyed or low-alloyed carbon steels.

9. The method according to any one of the preceding claims, characterized marked 5 net, that the cooling in the cooling station (14) the starting material (17) before

Rolling (7) to a temperature for adjusting an austenite microstructure only a little bit above the A ₃ temperature, for C 75 to a temperature of about 800 ⁰ C cools.

10. The method according to any one of claims 1 to 8, characterized in that the cooling in the cooling station (14) the starting material (17) before rolling zen (7) to a temperature for setting a Patentiergefüges, for C 75 on a Temperature between 400-550 ⁰ C cools.

11. The method according to any one of claims 1 to 8, characterized in that the cooling in the cooling station (14) the starting material (17) in front of WaI- zen 5 (7) to a temperature for setting a Bainitgefüges, for C 75 on a Temperature between 275-37O ⁰ C cools.

12. The method according to any one of claims 1 to 8, characterized in that the cooling in the cooling station (14) the starting material (17) before rolling zen (7) to a temperature for setting a supercooled Austenitgefü- o, for C 75 to a temperature between 220-280 ⁰ C cools.

13. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that the starting material (17) during the rolling process (7) at least on the after cooling of the starting material (17) in the cooling station (14) eingestell¬ th temperature is maintained.

5 14. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that the starting material (17) after the roll forming (7) for near-net flat profile (18) of a further cooling (9, 10), in particular ei¬ ner rapid cooling (10 ) is subjected.

15. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that the rapid cooling (10) the rolled flat profile (18) at least below the temperature limit for the course of oxidation processes on the Ober¬ surface of the flat profiles (18) cools.

5 16. The method according to claim 9, characterized in that after rolling zen (7) of the flat profile (17) in the temperature range of Austenitgefüges directly followed by a cooling of Austenitgefüges for conversion into a Sor- bitgefüge is performed.

17. The method according to claim 12, characterized in that after the o rollers (7) of the flat profile (17) in the temperature range of the supercooled

Austenite microstructure and the cooling in a cooling section (9, 10) with a deterio- ration of the supercooled austenite microstructure for conversion into a martensite microstructure directly followed by a tempering treatment with a cooling of the flat profile (18) before winding.

5 18. The method according to claim 12, characterized in that after rolling (7) of the flat profile (18) in the temperature range of supercooled Au¬ stenitgefüges directly followed by a treatment without Abschre¬ ckung the supercooled Austenitgefüges, but with a tempering treatment to form a Bainitgefüges and a tempering treatment is performed with cooling o of the flat profile (18) before winding (11).

19. Method according to claim 12, characterized in that after rolling (7) of the flat profile (18) in the temperature range of the austenitic structure a quenching of the austenite microstructure for conversion into a martensite microstructure is carried out and then a tempering treatment with a cooling 5 of the flat profile (18 ) is performed before winding (11).

20. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that the cooling of the starting material (17) after passing through the Auf¬ heating station (5) and before the rolling (7) in a tempered metal bath (14).

21. The method according to claim 20, characterized in that for the cooling of the starting material (17) after passing through the heating station (5) the Vorma¬ material (17) remains a predetermined time in the tempered metal bath (14), in particular the tempered metal bath ( 14) passes through a predetermined time.

22. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that the heating (5) of the starting material (15) by means of inductive heating and / or conductive heating (16) and / or by means of liquid metal baths er¬ follows.

23. The method according to any one of the preceding claims, characterized marked, that the heating (5) of the starting material (1) under protective gas influence (6) is performed.

24. The method according to any one of the preceding claims, characterized gekennzeich¬ net, that between the heating station (5) and the cooling station (14) is a Gleichmäßi- gungserinrichtung (12) for a temperature compensation within the heated starting material (17).

25. The method according to claim 24, characterized in that the Vergleich¬ moderate temperature within the heated starting material (17) after passing through the heating station (5) under protective gas influence (12) durchge leads.

26. Device (1) for carrying out a method according to claim 1, da¬ characterized in that the device (1) in the passage direction of Vor¬ material (17) a winding / withdrawal device (2, 3) for the unwinding of the windable starting material (17) or a feeding device for the bar-shaped starting material, a heating station (5), a cooling station (14) for setting a rolling temperature, a rolling station (7), a cooling section (9, 10) and a winding / extraction device (11) auf¬ for winding the windable Flach¬ profile (18) or a discharge device for the rod-shaped flat profile.

27. Device (1) according to claim 26, characterized in that the rolling station (7) has at least one rolling device, preferably a plurality of rolling devices connected one behind the other.

28. Device (1) according to one of claims 26 or 27, characterized in that in the region of the at least one rolling device (7) temperature monitoring (8) for detecting the temperature of the starting material (17) before / and / or after the rollers is arranged.

29. Device (1) according to one of claims 26 to 28, characterized gekenn¬ characterized in that for heating the Vormaterials (17) by means of conductive heating current-carrying contact rollers (16) in the inlet region of Vorrich¬ device (1) for the starting material (17 17) are arranged.

30. Device (1) according to any one of claims 26 to 29, characterized gekenn¬ characterized in that the cooling station (14) for adjusting a rolling temperature has a temperature-controlled metal bath.

31. Device (1) according to claim 30, characterized in that the tem¬ perierte metal bath (14) is a metal bath of a lead-bismuth alloy.

32. Device (1) according to one of claims 30 or 31, characterized gekenn¬ characterized in that the tempered metal bath (14) before and / or after the Walzstati¬ on (7) is arranged.

33. Device (1) according to any one of claims 30 to 32, characterized gekenn¬ characterized in that the tempered metal bath (14) has a winding and / or Umlenk¬ device (15) via which the starting material (17) during the dwell ¬ duration in temperature-controlled metal bath (14) is feasible.

34. Device (1) according to any one of claims 27 to 33, characterized in that in the cooling section (9, 10) a water cooling (10) cools the Flach¬ profile (18) with a high temperature gradient.

35. Device (1) according to any one of claims 27 to 34, characterized gekenn¬ characterized in that for heating the flat profile (18) for a after rolling (7) subsequent tempering a further conductive heating station (5 ^' ) is providable.

36. Device (1) according to claim 35, characterized in that the Er¬ heating (5 ^' ) of the flat profile (18) for the annealing under inert gas influence (6).

37. Device (1) according to any one of claims 27 to 36, characterized gekenn¬ characterized in that for cooling the flat profile (18) in the context of a after rolling (7) subsequent tempering a further cooling section (10) is providable.

38. Flat profile (18), produced by the method according to claim 1.

39. Flat profile (18) according to claim 38, characterized in that the

Flat profile (18) has a rectangular cross-section or a rectangular cross-section.

40. Flat profile (18) according to any one of claims 38 or 39, characterized in that as the starting material (17) typical carbon steels, in particular

Carbon steels having a carbon content between 0.10 and 1.35%, in particular C 10 to Ck 101/125 Cr1, are processable.

41. Flat profile (18) according to any one of claims 38 to 40, characterized gekenn¬ characterized in that the flat profile (18) in dimensions between 0.5 - 5 mm thickness and 4 - 25 mm width can be processed.