EP1795617A1 - Procédé de traitement thermique pour tôles magnétiques - Google Patents

Procédé de traitement thermique pour tôles magnétiques Download PDF

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Publication number
EP1795617A1
EP1795617A1 EP06125750A EP06125750A EP1795617A1 EP 1795617 A1 EP1795617 A1 EP 1795617A1 EP 06125750 A EP06125750 A EP 06125750A EP 06125750 A EP06125750 A EP 06125750A EP 1795617 A1 EP1795617 A1 EP 1795617A1
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EP
European Patent Office
Prior art keywords
cooling
temperature
stage
steel strip
annealing
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP06125750A
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German (de)
English (en)
Other versions
EP1795617B1 (fr
EP1795617B9 (fr
Inventor
Jürgen Prof. Dr.-Ing. Schneider
Karl Dipl.-Phys. Telger
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel AG
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Priority to PL06125750T priority Critical patent/PL1795617T3/pl
Priority to SI200631780T priority patent/SI1795617T1/sl
Publication of EP1795617A1 publication Critical patent/EP1795617A1/fr
Publication of EP1795617B1 publication Critical patent/EP1795617B1/fr
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Publication of EP1795617B9 publication Critical patent/EP1795617B9/fr
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    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the invention relates to a method for heat treating steel strips consisting of a steel, the Si and / or Al, with the proviso that for the Si content% Si and the Al content% Al% Si + 2 x% Al ⁇ 6 , 6 wt .-%, up to 2.5 wt .-% Mn, optionally one or more elements from the group "P, Cr, Ni" in each case up to 1 wt .-%, optionally one or more elements from the group "C, N, S” with contents of up to 0.1 wt .-% and the remainder containing iron and unavoidable impurities are produced, in which the steel strips are first pass annealed and then cooled controlled in at least three stages , Such a method is for example from the EP 0 357 797 A1 known.
  • Steel strips made in long lengths and large widths are used in a very large area as construction materials. In a thickness range of about 0.1 to 2 mm uniform mechanical properties are required for such steel strips. These are achieved in part only after a heat treatment with subsequent forming.
  • the heat treatment usually includes annealing and controlled cooling. The annealing and cooling lead in practice to uneven planes and internal stresses of the band.
  • electrotechnical steels are in the field of motors for driving machines and vehicles as well as in the field of the transformation of energy between different electrical voltage levels. They are used here as an iron core for guiding the magnetic flux in the form of stacked electric sheet metal lamellae.
  • special low-loss varieties have been developed. These are essentially grain oriented materials that are characterized by banded Goss oriented textures. They are produced in complex processes with silicon contents of about 3% by weight. These materials are only mentioned here, but not further treated.
  • the soft and ferromagnetic materials are of great importance in electrical engineering and are used here eg for energy transformation and in the field of actuators (motors).
  • highly permeable materials in their amorphous, nanocrystalline or crystalline state are mentioned, all of which are generated in a coordinated manner, good conducting properties in the soft magnetic core for the provide magnetic flux. It is important to minimize the coercivity and to maximize the polarization even with low field requirements. This results in low core losses for small core sizes with low copper requirements for the windings.
  • a special economic importance in the case of soft magnetic materials is occupied by the silicon-alloyed steels.
  • a group of these steels is partially deformed at the steel strip producer in the finishing stand and / or in the stretch leveler and delivered to the customer in the so-called semi-finished state.
  • sheet metal parts are punched or cut from the semi-finished material, which are subsequently annealed. Only after this annealing, the required good soft magnetic properties set.
  • the other group of these electrotechnical steels which is called “fully-finished" is already heat treated at the steel strip producer prior to delivery to the customer so that it has the required magnetic Retains properties even after punching or cutting at the customer, without the need for a final annealing must be carried out at the customer.
  • a "fully finished material” increasing the efficiency of further processing requires a good flatness before and after the punching process.
  • the present invention has therefore dealt in particular with the heat treatment carried out in the course of the production of fully-finished electrical tapes and has answered the question of how annealing with subsequent cooling is to be carried out in order to ensure good flatness states in the case of electrical sheet material at low internal stresses.
  • the "cooling gradients" CR1, CR2 and CR3 denote the temperature decreases per unit time [° C / s] which are achieved in the respective cooling stage (CR1, CR2, CR3 in each case ⁇ 0 ° C / s).
  • the invention is based on the finding that, in the conventional manufacture of electrical steel, inhomogeneous temperature conditions over the bandwidth during continuous annealing are the primary cause for the development of deviations in planarity and internal stresses. These are not only to a limited extent due to inhomogeneities in the temperature distribution in the furnace cross-section, but result essentially from the surface quality and the applied pass schedule during cold rolling. Here are playing when heating due to high Heat transfer coefficients remaining partial oxide layers from the pre-process (hot strip, cold strip) a strong role.
  • the roughness index RPc roughness peak number controls, in addition to the alloy composition of the surface, the energy absorption of the material surface primarily at relatively constant mean roughness depths.
  • the resulting small changes in the emission number are sufficient to trigger a further change in the emission number via the temperature dependence.
  • the cold rolling process provides the recrystallization nuclei and thus the starting point for a uniform or uneven recrystallization.
  • Inhomogeneous microstructural conditions over the bandwidth are thus due to high shear during cold rolling due to high Frictions on the surface caused.
  • Good homogeneously pickled surfaces without residual oxide layers are thus important prerequisites for a favorable homogeneous cold rolling and a low stress level of the material after annealing.
  • the cold rolling step can not eliminate these structural states or residual scale surfaces. On the contrary, in the case of severely shearing cold rolling conditions and high rolling forces in the sense of dislocation inhomogeneities, it only creates worse starting conditions for the recrystallizing continuous annealing. All this can cause z. B. in the middle and edge region during continuous annealing fluctuations of grain size distributions but also of coercive force values arise, which are then a sign of high internal stresses.
  • the respective surface quality and the grain size distribution of the cold rolling process could be identified as a significant influence on the homogeneity of a strip with regard to low internal stresses and good flatness.
  • the invention has now shown a way in which the generation of internal stresses and flatness problems in the manufacture of steel strips of the type in question can be minimized without the need to change the cold rolling process or the other process steps preceding the heat treatment step mentioned above.
  • the critical areas for elongation in continuous annealing lie in two areas of cooling.
  • On the one hand in the range of the Curie temperature, which leads by the anomalies of the specific heat capacity and the emission behavior to the temperature-dependent utilization of the irradiated heat energy.
  • the construction of the ferromagnetic coupling of the atoms during the cooling process costs energy that is not available for lowering the temperature.
  • a previously existing small temperature difference in band areas across the bandwidth can be excited to a significant increase.
  • the two main influencing factors in the temperature transfer, emission number and specific heat capacity are temperature-dependent here and contribute in an unfavorable case to a mutual influence and to create significantly different values across the bandwidth. Due to the resulting temperature difference results in evaluation of the resulting due to the local temperature difference across the bandwidth different expansions, which are also temperature-dependent, and the band trains, which add up in "colder", shorter band areas, a transformation of the material.
  • the stresses arising in the course of the heat treatment according to the invention could be detected by means of magnetic measurements, in particular the coercive force.
  • An adaptation of the annealing curve in this temperature range of the cooling in the form of a lying at 730 - 750 ° C (740 ° C, the Curie temperature of this alloy) temperature maintenance level showed a significant improvement in the magnetic properties compared to the driving without the inventive cooling stop. This is especially true if inhomogeneous roughness profiles across the bandwidth were measured.
  • the roughness profiles of the cold-rolled behave Material with respect to average surface roughness and roughness peak number almost identical, so that after the non-oxidizing annealing, the panel samples could be used after the annealing for comparison.
  • the cooling can be accelerated during the third stage.
  • the duration of the third stage of cooling is 14-30 seconds.
  • a further advantageous embodiment of the invention is characterized in that the cooling from a 5 - 10 seconds before reaching the Curie temperature T C lying time and up to a 5 - 10 seconds after reaching the Curie temperature T C lying time with a Cooling gradient CR 2 is set near the minimum cooling gradient CR 2MIN .
  • the construction of thermal stresses in the material is reliably prevented, which may otherwise occur due to the non-linear in the critical temperature range of T C specific heat capacity of the processed sheet metal material.
  • the structure of the ferromagnetic order taking place in the region of the Curie temperature requires energy which is then not available for changing the temperature.
  • the potential for the generation of internal stresses is thus minimized.
  • An oxidation of the steel strip during annealing can also be avoided in the procedure according to the invention in that the continuous annealing is carried out under a protective gas atmosphere.
  • This protective gas atmosphere can also decarburizing in a manner known per se in order to achieve minimized C contents in the finished steel strip.
  • the steel strip is heated to the annealing temperature during continuous annealing in a single heating stage.
  • a rapid heating device can be used to heat the steel strip, which heats the steel strip in the range of 20 - 450 ° C in an open-heated combustion gas atmosphere at a heating rate of more than 100 ° C / s.
  • the rapid heating causes a surface oxidation that makes the energy absorption uniform throughout the annealing process, thus minimizing temperature differences across the bandwidth.
  • the heating of the steel strip to the annealing temperature is carried out in at least two stages. This ensures uniform heating of the steel strip to maximum temperature.
  • the method according to the invention is particularly suitable for steel strips made of steels with Si contents% Si and Al contents% A1, for which% Si + 2 ⁇ % A1 ⁇ 6.6% by weight, and their mean specific Heat capacity C P at T c shows a non-linear increase.
  • the inventive method has a higher tolerance width over the bandwidth on the top and bottom surface fluctuating surface roughness.
  • low internal stress and a good flatness ensure fluctuate in which the width of the bands Rauheitsspitzenbib (RPc) from 100 to 300, and R z values from 2 to 7 microns.
  • the invention enables low magnetic scattering (standard deviation) below 1.0% for the coercive field strength change by subsequent stress relief annealing at 650 ° C versus annealing without holding steps.
  • the invention gave higher permeability values at 1.0 and 1.5 T polarization over conventionally processed steel strip.
  • Particularly advantageous permeability values at 1.0 and 1.5 T polarization with an improvement of up to 20% can be achieved with processing according to the invention for electro-sheet alloys for whose Si content% Si and Al content% Al is 0.9% by weight. % ⁇ % Si + 2 x% Al ⁇ 1.8 wt%.
  • heat-treated steel strip according to the invention regularly has up to 40% lower coercive field strength values at 2500 and 5000 A / m for the annealed material compared to the linear standard cooling (without cooling stop according to the invention).
  • material cooled after annealing has a greater tolerance to material that has been conventionally cooled linearly with respect to the influence of carbon residue levels on magnetic aging.
  • material produced according to the invention only a max. 5% higher re-magnetization loss compared to 10-20% increase in the re-magnetization loss occurring in conventional cooling processes.
  • the carbon content is limited to less than 30 ppm, and it has been found that in the case of electrical steel sheets for whose S content% Si and Al content% Al% Si + 2 x% Al ⁇ 1.8 Wt .-%, the improvement of the invention also sets at carbon contents of up to 50 ppm.
  • the conventionally constructed plant A for heat treatment of a cold-rolled steel strip S comprises in the direction of belt B successively a coiler C, an inlet storage D, a continuous furnace E, connected to the continuous furnace E cooling device F, a discharge storage G and a coiler H.
  • the continuous furnace E is divided into 26 successively traversed in the strip running direction B, in each case immediately merging into one another furnace zones 1 to 26, of which the furnace zone 1 to the kiln inlet E and the furnace zone 26 is assigned to the kiln outlet E from.
  • the furnace zones 1 to 12 form a jet tube heating section E A
  • the furnace zones 13 - 26 together form a radiation cooling section E K.
  • Each individual furnace zone 1-26 is controllable with respect to the temperatures T o prevailing in it.
  • the cooling device F which is connected directly to the outlet of the continuous furnace E is designed in a manner also known per se as a protective gas jet rapid cooling device.
  • Appendix A 0.5 mm thick and 1265 mm wide cold-rolled steel sheet steel strips were produced, which were produced from a steel alloy which in a first example (Example 1) 1.3 wt.
  • each of the steel alloys further contained in total up to 1% by weight contents of Mn, P, Cr, Ni and in total up to 0.1% by weight of Al. % Contents of C, N, S, balance iron and unavoidable impurities had.
  • the correspondingly assembled strips were first hot rolled in a conventional manner to hot strips and then cold rolled in the same conventional manner to final thickness.
  • the supplied as coils I, cold-rolled steel sheet steel steel strips S are unwound in the Abhaspel Rhein C and passed over the tape storage D in the continuous furnace E. There, they were first heated in the first 12 furnace zones 1 to 12 until they had a uniform temperature of at least 800 ° C. when leaving the furnace zone 12 over their strip cross-section.
  • the control of the respective furnace temperature T o in the furnace zones 1 to 12 was carried out so that the temperature at the entrance of the steel strip S in the furnace zone 13 above the critical Curie temperature T C was, in Example 1 740 ° C, in Example 2 746 ° C and 3 767 ° C in Example.
  • the respective strip temperature T B is plotted over the furnace zones 1 to 26.
  • the entries relating to the heat-treated steel strip S E according to the invention are characterized by unfilled squares.
  • steel strip S K applied the respective strip temperature T B over the furnace zones 1 to 26.
  • the temperature values determined for the conventionally heated and cooled steel strip S K are indicated by circles.
  • the temperature gradients CR 1 , CR 2 , CR 3 set in inventive and conventional heat treatment are given in the following table.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP06125750.7A 2005-12-09 2006-12-08 Procédé de traitement thermique pour une tôle magnétique Active EP1795617B9 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PL06125750T PL1795617T3 (pl) 2005-12-09 2006-12-08 Sposób obróbki cieplnej taśmy stalowej na blachy elektrotechniczne
SI200631780T SI1795617T1 (sl) 2005-12-09 2006-12-08 Postopek za toplotno obdelavo jeklenega traku iz elektroploäśevine

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
DE102005059308A DE102005059308A1 (de) 2005-12-09 2005-12-09 Verfahren zum Wärmebehandeln eines Stahlbands

Publications (3)

Publication Number Publication Date
EP1795617A1 true EP1795617A1 (fr) 2007-06-13
EP1795617B1 EP1795617B1 (fr) 2014-02-26
EP1795617B9 EP1795617B9 (fr) 2014-10-29

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ID=37903808

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EP06125750.7A Active EP1795617B9 (fr) 2005-12-09 2006-12-08 Procédé de traitement thermique pour une tôle magnétique

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EP (1) EP1795617B9 (fr)
DE (1) DE102005059308A1 (fr)
ES (1) ES2464865T3 (fr)
PL (1) PL1795617T3 (fr)
SI (1) SI1795617T1 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115058582B (zh) * 2022-07-14 2024-06-11 上海曙佳科技发展有限公司 一种连退炉炉内可视化及工件温度管理方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3130088A (en) * 1958-12-31 1964-04-21 Armco Steel Corp Thermal-flattening of metallic strip
DE1583349A1 (de) * 1966-08-09 1973-08-16 Creusot Loire Verfahren zur verbesserung der magnetischen eigenschaften von staehlen fuer magnetische zwecke und nach dem verfahren behandelte staehle
JPS5296919A (en) 1976-02-10 1977-08-15 Kawasaki Steel Co Annealing of non anisotropic silicon steel sheets
EP0357797A1 (fr) 1988-03-04 1990-03-14 Nkk Corporation Procede de production de feuilles d'acier non oriente presentant d'excellentes proprietes magnetiques dans un champ faiblement magnetique
JPH04221019A (ja) * 1990-12-19 1992-08-11 Sumitomo Metal Ind Ltd 厚板電磁軟鉄の製造方法
EP0538519A1 (fr) * 1991-10-21 1993-04-28 ARMCO Inc. Procédé de fabrication d'acier ordinaire à haute teneur en silicium, à basse teneur en carbone et à grains orientés

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3130088A (en) * 1958-12-31 1964-04-21 Armco Steel Corp Thermal-flattening of metallic strip
DE1583349A1 (de) * 1966-08-09 1973-08-16 Creusot Loire Verfahren zur verbesserung der magnetischen eigenschaften von staehlen fuer magnetische zwecke und nach dem verfahren behandelte staehle
JPS5296919A (en) 1976-02-10 1977-08-15 Kawasaki Steel Co Annealing of non anisotropic silicon steel sheets
EP0357797A1 (fr) 1988-03-04 1990-03-14 Nkk Corporation Procede de production de feuilles d'acier non oriente presentant d'excellentes proprietes magnetiques dans un champ faiblement magnetique
JPH04221019A (ja) * 1990-12-19 1992-08-11 Sumitomo Metal Ind Ltd 厚板電磁軟鉄の製造方法
EP0538519A1 (fr) * 1991-10-21 1993-04-28 ARMCO Inc. Procédé de fabrication d'acier ordinaire à haute teneur en silicium, à basse teneur en carbone et à grains orientés

Also Published As

Publication number Publication date
EP1795617B1 (fr) 2014-02-26
PL1795617T3 (pl) 2014-08-29
DE102005059308A1 (de) 2007-06-14
SI1795617T1 (sl) 2014-06-30
ES2464865T3 (es) 2014-06-04
EP1795617B9 (fr) 2014-10-29

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