EP0619376B1 - Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten - Google Patents

Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten Download PDF

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Publication number
EP0619376B1
EP0619376B1 EP94103908A EP94103908A EP0619376B1 EP 0619376 B1 EP0619376 B1 EP 0619376B1 EP 94103908 A EP94103908 A EP 94103908A EP 94103908 A EP94103908 A EP 94103908A EP 0619376 B1 EP0619376 B1 EP 0619376B1
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EP
European Patent Office
Prior art keywords
temperature
hot
strip
slabs
rolled
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.)
Expired - Lifetime
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EP94103908A
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German (de)
English (en)
French (fr)
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EP0619376A1 (de
Inventor
Fritz Dr. Dipl.-Phys. Bölling
Andreas Dr. Dipl.-Phys. Böttcher
Manfred Dr. Dipl.-Ing. Espenhahn
Christof Dipl.-Phys. Holzapfel
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Thyssen Stahl AG
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Thyssen Stahl AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • 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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • 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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling

Definitions

  • the invention relates to a process for the production of grain-oriented electrical sheets with a finished strip thickness in the range from 0.1 to 0.5 mm, in which more than 0.005% to 0.10% C, 2.5 to 6%, produced by continuous casting, Slabs containing 5% Si and 0.03 to 0.15% Mn are first heated through at a reduced temperature in one or two stages and then pre-rolled and hot-rolled to the final hot strip thickness, and then the strips hot-rolled to the final thickness are annealed and cooled in an accelerated manner and cold-rolled to the finished strip thickness in a cold-rolling stage or in a plurality of cold-rolling stages, and the cold-rolled strips are then subjected to recrystallizing annealing in a humid H 2 and N 2 atmosphere with simultaneous decarburization, and the application of an essentially MgO-containing release agent to both sides of the cold strip surface , a high temperature annealing and finally a final annealing with an insulation b be subjected to stratification.
  • Slabs preferably continuous cast slabs with a thickness in the range of approximately 150 to 250 mm, which is usually 0.025 up to 0.085% C and 2.0 to 4.0% Si as well as manganese, sulfur, possibly Contain aluminum and nitrogen before hot rolling in one or in two stages to a temperature of the order of magnitude from 1350 ° C to max.
  • This measure serves the purpose of being used as grain growth inhibitors known and as the control phase in high-temperature annealing (Secondary recrystallization) acting particles, e.g. Sulfides (MnS) and nitrides (AlN), completely dissolved.
  • the second heating stage up to a temperature of max. 1450 ° C and one Warm the slabs at this temperature to then the slabs already reduced in thickness to hot strip with a final thickness in the range of 1.5 to approx. 5 mm, max. to Roll 7 mm warm and finished.
  • DE-C2 29 09 500 describes a process for the production known from grain-oriented electrical sheets, in which the slabs containing 2.0 to 4.0% Si, up to 0.085% C and up to Contain 0.065% Al or another known inhibitor, before hot rolling in one step to a temperature of at least 1300 ° C, preferably greater than 1350 ° C, heated and heated through at this temperature, i.e. a sufficient time be kept long. This should prevent the inhibitors from Hot rolling completely dissolved and not eliminated prematurely to prevent the hot rolling from large and coarse excretions arise.
  • An excretion of the inhibitors also during the subsequent one Avoiding hot rolling is accordingly known in this Process provided that the hot rolling at least one recrystallization rolling during finish rolling with at least a stitch decrease of more than 30% in a temperature range from 960 ° C to 1190 ° C, namely expressis verbis with the Provided that the inhibitors do not fail during hot rolling. Elimination of the inhibitors and especially one Coarsening of the particles that may have been excreted are subsequently this known method preferably avoided 'when the recrystallization rolling of the previously at a temperature of at least 1350 ° C through heated slabs in the temperature range from 1050 ° C to 1150 ° C is carried out.
  • the slabs are made in the usual way Hot-rolled, the hot-rolled strip is heat-treated or annealed and then also in a conventional manner in one step or cold rolled to the final sheet thickness in two stages.
  • the cold-rolled strip is then annealed for decarburization Connect a release agent to both sides of the cold strip surface applied and finally a high temperature annealing subjected to secondary recrystallization.
  • (Si, Al) N particles are apparently only used as inhibitors effective or the grain-oriented electrical sheets with the desired magnetic properties can only be produced when the cold rolled strip at the end of primary recrystallization and decarburization annealing and before introduction secondary recrystallization of nitriding, i.e. one additional further process step is subjected.
  • S can contain aluminum nitrides during solution treatment of the Slabs can only be brought into solution incompletely.
  • the necessary Inhibitors are therefore used after decarburization annealing - As in the known from EP-B1 0 219 611 Process - by embroidery or nitriding of the tape. This can be done by setting, for example a special ammonia-containing gas atmosphere after the Decarburization annealing and before high temperature annealing and / or by adding nitrogen-containing compounds to the im essential release agents containing MgO (e.g. according to EP-A1 0 339 474, EP-A1 0 390 142).
  • EP-B1 0 098 324 and EP-A2 0 392 535 known in which the heating temperature is below 1280 ° C and an additional process step, e.g. the Nitriding, is not absolutely necessary.
  • Stabilizing the According to EP-A2 0 392 535, secondary recrystallization is carried out by Setting the hot rolling parameters, such as final hot rolling temperature, Degree of deformation (based on the last three hot rolling passes) or reel temperature reached. Following EP-B1 0 098 324 this stabilization will be achieved through the coordination of the Annealing conditions that reach hot rolling and cold rolling parameters.
  • the object of the invention is to improve the method of the type mentioned at the outset with the advantageously reduced temperature for the solution annealing of the slabs in such a way that for the magnetic properties of the electrical sheets, in particular for the magnetic reversal losses P 1.7 / 50 , more favorable values can be achieved without using further process steps.
  • this object is achieved in the method of the beginning mentioned type through the measures and procedural steps (1) to (4) of claim 1 solved.
  • the slabs in addition to the usual nitrogen content in the range of 0.0045 to 0.0120% additionally 0.020 to 0.300% Cu and more than Contain 0.010% S, but less than 0.035% Al.
  • the method steps (2) and (3) that manganese sulfides are practically not brought into solution and therefore mostly as coarse after hot rolling Particles are present.
  • RGO Regular Grain Oriented
  • the invention By heating the slabs according to (2) that aluminum nitrides only to a small extent be brought into solution and therefore also predominantly after hot rolling according to (3) excreted as coarse particles. This one too Share can no longer in the subsequent procedural steps act as an inhibitor.
  • HGO High-permeability Grain Oriented
  • crucial grain growth inhibitor Precipitated copper-sulfide particles are with an average diameter of less than about 100 nm, preferably less than 50 nm, in the following Stages or procedural steps the actual, essential and represent effective tax phase. Only one more small proportion after the process step according to the invention (4) also separated and finely divided aluminum nitrides effective as an inhibitor. This is particularly evident non-inventive comparative examples by the inventive Procedure with otherwise identical features and procedural steps is applied to slabs, but only one Have a sulfur content of less than 0.005%. In these cases there are no sufficient particles acting as inhibitors large number before.
  • the slabs contain approx. 0.010 to 0.065% Al
  • the slabs also before the hot rolling at a temperature of the order of magnitude of about 1400 ° C, are hot inhibitors by the hot rolling and subsequent hot strip annealing are finely divided AlN particles and such electrical sheets preferably have a magnetic induction B 8 greater than 1.88 T.
  • grain-oriented electrical sheets can now be produced using the method according to the invention with the same magnetic induction B 8 in Tesla (T) as RGO and also HGO electrical sheets have with improved values for the magnetic loss P 1.7 / 50 in watts per kg (W / kg).
  • the method of the invention are first of all with the help of the known continuous casting process slabs with an initial thickness in the range of 150 to 300 mm, preferably in the Range from 200 to 250 mm.
  • the Slabs also known as thin slabs with an initial thickness in be in the range of approximately 30 to 70 mm.
  • Advantageously can be used in these cases during the production of the hot strip the process step (3) on the roughing to an intermediate thickness to be dispensed with.
  • Grain-oriented electrical sheets can also be used by the process according to the invention also from slabs or tapes with an even smaller starting thickness if using these slabs or tapes beforehand of the strip casting were generated.
  • the slabs, thin slabs or strips, hereinafter briefly slabs named and so defined contain the in the preamble and in characterizing part of claim 1 specified content of carbon, silicon, manganese, nitrogen and copper as well compared to the prior art (according to EP-B1 0 219 611) the sulfur content according to the invention in the range from more than 0.010, preferably greater than 0.015%, up to 0.050% and the one specifically lowered into the lower known area Aluminum content in the range from 0.010 to 0.030%, max. up to 0.035%, balance Fe including impurities.
  • the contents specified in claim 2 adjusted to aluminum and sulfur.
  • the salary too the remaining alloy components are preferably for each Alloy element individually or in combination within the areas specified in claim 2.
  • composition tin up to 0.15%, but preferably only 0.02-0.06%, be added. This will make the magnetic properties not further improved.
  • Figures 1, 2 and 3 illustrate the solution behavior for grain-oriented electrical sheets with usual Si contents. The contents taken into account correspond to the exemplary embodiments shown in Tables 1, 2 and 3.
  • Carrying out process step (2) causes that heating of the slabs before hot rolling manganese sulfides practically cannot be brought into solution. Because the corresponding Solubility curves for aluminum nitride the solubility curves are similar or comparable for manganese sulfides already in the heating of the slabs according to the invention the majority of aluminum nitrides excreted. After completing this step practically only copper sulfides are almost completely in solution.
  • Method step (3) may be dependent first from the initial thickness of the slabs in 3 to 7 stitches pre-rolled and then in 5 to 9 passes to the final hot strip thickness in the range from 1.5 to 5 mm, max. up to 7 mm finish rolled.
  • the slabs are pre-rolled with a Initial thickness in the range of 150 to 300 mm, preferably in the range from 200 to 250 mm, except for a pre-strip thickness in the range of approx. 30 to 60 mm. Overall, the number of Stitches during roughing and finish rolling according to the starting thickness of the slabs and according to the desired one Final hot strip thickness.
  • the essential feature of process step (3) is, however, that the strips with the lowest possible final rolling temperature in the range of 880 ° C to 1000 ° C, preferably in the range from 900 ° C to 980 ° C.
  • the lower limit determined by the fact that there is still a problem-free deformation or rolling the strips without any difficulties, such as. Strip unevenness and strip profile deviations, must be possible.
  • Hot rolling is more than 60% of the total nitrogen content bound to aluminum in the form of AlN.
  • a Measure of the amount of nitrogen present in aluminum is the N-Beeghley value.
  • Table 4 illustrates how the invention Process the type and size of the excretions, and thus their Effectiveness as an inhibitor. It also shows the differences from the present excretions, the achieved by methods according to the state of the art (HGO, RGO) will.
  • cold rolling takes place the tapes preferably in one step to the finished tape thickness in the range of 0.1 to 0.5 mm.
  • the final hot strip thickness can be cold rolled according to claim 6 also take place in two stages, according to claim 7 before the first cold rolling stage is preferably preheated becomes. This contributes to stabilization in an advantageous manner secondary recrystallization in the subsequent high-temperature annealing at.
  • the recrystallizing and decarburizing annealing of the strips is carried out at a temperature in the range from 750 ° C. to 900 ° C., preferably at a temperature in the range from 820 ° C. to 880 ° C, in a humid atmosphere containing H 2 and N 2 .
  • a glow separator containing primarily MgO is then applied.
  • the strips are then in a known manner in a long-term hood annealing with a slow heating of 10 to 100 K / h, preferably 15 to 25 K / h, to at least 1150 ° C at this temperature in an atmosphere consisting of H 2 and N 2 annealed and slowly cooled again after holding for 0.5 to 30 h.
  • the insulation coating which is also known, is carried out with the associated final annealing.
  • Table 1 shows the results using eight exemplary embodiments when using the method according to the invention Claim 1 on slabs with an initial thickness of 215 mm.
  • Table 2 shows further results, that according to the inventive method according to claim 1 in combination with the procedural steps according to the subclaims 6 and 7 can be achieved.
  • the cold rolling took place in these cases in two stages without and also with the preheating before the first cold rolling stage according to claim 7.
  • grain-oriented electrical sheets can be produced which have a magnetic induction B 8 , as they also have grain-oriented electrical sheets of both the RGO grade and the HGO grade.
  • these grades are now only achieved by using a single method with the method steps specified in claim 1.
  • values which are substantially more favorable for the associated magnetic reversal losses are advantageously achieved. This is illustrated in FIG.
  • FIG. 4 shows the corresponding and typical value pairs for grain-oriented electrical sheets of the RGO and HGO grades, which until now could only be produced in a known manner using two separate, different processes.

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  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
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EP94103908A 1993-04-05 1994-03-14 Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten Expired - Lifetime EP0619376B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE4311151 1993-04-05
DE4311151A DE4311151C1 (de) 1993-04-05 1993-04-05 Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten

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EP0619376A1 EP0619376A1 (de) 1994-10-12
EP0619376B1 true EP0619376B1 (de) 1998-08-05

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EP94103908A Expired - Lifetime EP0619376B1 (de) 1993-04-05 1994-03-14 Verfahren zur Herstellung von kornorientierten Elektroblechen mit verbesserten Ummagnetisierungsverlusten

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US (2) US5711825A (ru)
EP (1) EP0619376B1 (ru)
JP (1) JP2728112B2 (ru)
KR (1) KR100247598B1 (ru)
CN (1) CN1040998C (ru)
AT (1) ATE169346T1 (ru)
AU (1) AU673720B2 (ru)
BR (1) BR9401398A (ru)
CA (1) CA2120438C (ru)
CZ (1) CZ282649B6 (ru)
DE (2) DE4311151C1 (ru)
ES (1) ES2121590T3 (ru)
HU (1) HU216760B (ru)
PL (1) PL173284B1 (ru)
RO (1) RO114637B1 (ru)
RU (1) RU2126452C1 (ru)
SK (1) SK281614B6 (ru)

Cited By (2)

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DE102011054004A1 (de) 2011-09-28 2013-03-28 Thyssenkrupp Electrical Steel Gmbh Verfahren zum Herstellen eines kornorientierten, für elektrotechnische Anwendungen bestimmten Elektrobands oder -blechs
CN110218850A (zh) * 2019-06-24 2019-09-10 鞍钢股份有限公司 一种降低取向硅钢高温退火边部粘结缺陷的隔离剂

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DE19628136C1 (de) * 1996-07-12 1997-04-24 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech
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IT1284268B1 (it) * 1996-08-30 1998-05-14 Acciai Speciali Terni Spa Procedimento per la produzione di lamierino magnetico a grano orientato, con elevate caratteristiche magnetiche, a partire da
IT1285153B1 (it) * 1996-09-05 1998-06-03 Acciai Speciali Terni Spa Procedimento per la produzione di lamierino magnetico a grano orientato, a partire da bramma sottile.
IT1290171B1 (it) * 1996-12-24 1998-10-19 Acciai Speciali Terni Spa Procedimento per il trattamento di acciaio al silicio, a grano orientato.
IT1290173B1 (it) * 1996-12-24 1998-10-19 Acciai Speciali Terni Spa Procedimento per la produzione di lamierino di acciaio al silicio a grano orientato
IT1290978B1 (it) * 1997-03-14 1998-12-14 Acciai Speciali Terni Spa Procedimento per il controllo dell'inibizione nella produzione di lamierino magnetico a grano orientato
IT1290977B1 (it) * 1997-03-14 1998-12-14 Acciai Speciali Terni Spa Procedimento per il controllo dell'inibizione nella produzione di lamierino magnetico a grano orientato
FR2761081B1 (fr) * 1997-03-21 1999-04-30 Usinor Procede de fabrication d'une tole d'acier electrique a grains orientes pour la fabrication notamment de circuits magnetiques de transformateurs
AU2698897A (en) * 1997-04-16 1998-11-11 Acciai Speciali Terni S.P.A. New process for the production of grain oriented electrical steel from thin slabs
AU2698097A (en) * 1997-04-16 1998-11-11 Acciai Speciali Terni S.P.A. New process for the production at low temperature of grain oriented electrical steel
WO1998048062A1 (en) * 1997-04-24 1998-10-29 Acciai Speciali Terni S.P.A. New process for the production of high-permeability electrical steel from thin slabs
DE19735062A1 (de) * 1997-08-13 1999-02-18 Thyssen Stahl Ag Verfahren zur Herstellung von kornorientiertem Elektroblech und Verwendung eines Stahls für Elektroblech
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IT1299137B1 (it) * 1998-03-10 2000-02-29 Acciai Speciali Terni Spa Processo per il controllo e la regolazione della ricristallizzazione secondaria nella produzione di lamierini magnetici a grano orientato
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KR101683693B1 (ko) * 2013-02-27 2016-12-07 제이에프이 스틸 가부시키가이샤 방향성 전자 강판의 제조 방법
CN103484643B (zh) * 2013-08-23 2015-04-15 安阳钢铁股份有限公司 一种防止取向硅钢热轧边裂的方法
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CA2120438A1 (en) 1994-10-06
BR9401398A (pt) 1994-10-18
HUT70224A (en) 1995-09-28
JPH06322443A (ja) 1994-11-22
JP2728112B2 (ja) 1998-03-18
US5711825A (en) 1998-01-27
PL173284B1 (pl) 1998-02-27
DE4311151C1 (de) 1994-07-28
SK38894A3 (en) 1994-11-09
HU9400843D0 (en) 1994-06-28
HU216760B (hu) 1999-08-30
ATE169346T1 (de) 1998-08-15
CA2120438C (en) 2006-06-13
CN1098440A (zh) 1995-02-08
AU673720B2 (en) 1996-11-21
RU2126452C1 (ru) 1999-02-20
RO114637B1 (ro) 1999-06-30
RU94009842A (ru) 1996-06-27
US5759294A (en) 1998-06-02
EP0619376A1 (de) 1994-10-12
ES2121590T3 (es) 1998-12-01
CN1040998C (zh) 1998-12-02
KR100247598B1 (ko) 2000-04-01
CZ282649B6 (cs) 1997-08-13

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