EP2612942A1 - Non-grain oriented electrical steel or sheet metal, component produced from same and method for producing non-grain oriented electrical steel or sheet metal - Google Patents

Abstract

The non grain-oriented electrical steel strip or sheet comprises a steel in addition to iron and unavoidable impurities, silicon (2.4-3.4 wt.%), aluminum (2 wt.%), manganese (1 wt.%), carbon (0.006 wt.%), nitrogen (0.006 wt.%), sulfur (0.006 wt.%), titanium (0.1-0.5 wt.%), and phosphorus (0.1-0.3 wt.%), where a ratio of titanium to phosphorus is 1.43:1.67. The electrical steel strip or sheet has a hysteresis loss P(1/400) at a polarization of 1 tesla and a frequency of 400 Hz at a thickness of the electrical steel strip or sheet of 0.5 mm of 65 W/kg and at a thickness of 0.35 mm of 45 W/kg. Independent claims are included for: (1) a component for electrotechnical applications; and (2) a method for producing a non grain-oriented electrical steel strip or sheet.

Description

The invention relates to a non-grain oriented electrical steel strip or sheet for electrical applications, an electrical component made from such an electrical steel strip or sheet, and a method for producing an electrical steel strip or sheet.

Non-grain oriented electrical tapes or sheets, also referred to in the jargon as "NO electrical steel or sheet" or in the English language as "NGO-Electrical Steel" ("NGO" = Non Grain Oriented), are used to enhance the magnetic flux in Iron cores used by rotating electrical machines. Typical uses of such sheets are electric motors and generators.

In order to increase the efficiency of such machines, the highest possible speeds or large diameters of the components rotating during operation are sought. As a result of this trend, the electrically relevant, made of electrical tapes or sheets of the type in question here manufactured components are exposed to high mechanical stress, which is available from today often can not be met in standing NO-electrical steel grades.

From the US 5,084,112 For example, there is known a NO electric steel strip or sheet having a yield strength of at least 60 kg-f / mm ² (about 589 MPa) and made of a steel containing, in addition to iron and unavoidable impurities (in% by weight) to to 0.04% C, 2.0 - less than 4.0% Si, up to 2.0% Al, up to 0.2% P and at least one element from the group "Mn, Ni", wherein the Sum of the contents of Mn and Ni is at least 0.3% and at most 10%.

To achieve an increase in strength through the formation of carbonitrides, contains from the US 5,084,112 known steel at least one element from the group "Ti, V, Nb, Zr", wherein in the case of the presence of Ti or V, the Ti content% Ti and the V content% V with respect to the C content% C and the unavoidable N content% N of the steel should satisfy the condition [0.4x (% Ti +% V)] / [4x (% C +% N)] <4.0. The presence of phosphorus in the steel is also attributed a strength-increasing effect. However, the presence of higher levels of phosphorus is warned because they can cause grain boundary embrittlement. To counteract this serious problem, an additional B content of 0.001-0.007% is proposed.

The thus composed steel is according to the US 5,084,112 poured into slabs, which are then hot rolled into a hot strip, which optionally annealed, then pickled and then cold rolled to a cold-rolled strip of a given final thickness. Finally, the cold strip obtained is subjected to a recrystallizing annealing, in which it is annealed at a temperature of at least 650 ° C, but less than 900 ° C annealing temperature.

In the case of the simultaneous presence of effective levels of Ti and P as well as B, N, C, Mn and Ni in the steel, those according to the US 5,084,112 Although NO electrical steel strips or sheets produced yield strengths of at least 70.4 kg-f / mm ² (688 MPa). At the same time, with a sheet thickness of 0.5 mm and a polarization of 1.5 Tesla and a frequency of 50 Hz, the magnetization losses P _1.5 are at least 6.94 W / kg. Such high core losses are no longer acceptable for modern electrical engineering applications. Furthermore, in many such applications the Ummagnetisierungsverluste at higher frequencies of great importance.

Against this background, the object of the invention was to provide a NO electrical steel strip or sheet and a manufactured from such a sheet or strip component for electrical applications, the increased strength, in particular a higher yield strength, and at the same time has good magnetic properties, in particular a low loss of magnetization at high frequencies. In addition, a method for producing such a NO electrical strip or sheet should be given.

With respect to the NO electrical steel strip or sheet, this object has been achieved according to the invention in that the NO electrical steel strip or sheet has the composition specified in claim 1.

Accordingly, the solution according to the invention of the above-mentioned object with respect to the component for electrical applications is that such a component is produced from an electrical steel sheet or strip according to the invention.

Finally, the above-mentioned object has been achieved with respect to the method in that at least the steps specified in claim 9 are passed through in the production of an electrical strip or sheet according to the invention.

Advantageous embodiments of the invention are specified in the dependent claims and are explained below as the general inventive concept in detail.

A non-grain-oriented electrical steel strip or sheet for electrotechnical applications obtained in accordance with the invention is thus made from a steel consisting of (in% by weight) 1.0-4.5% Si, in particular 2.4-3.4% Si, to to 2.0% Al, in particular up to 1.5% Al, up to 1.0% Mn, up to 0.01% C, in particular up to 0.006%, particularly advantageously up to 0.005% C, up to 0, 01% N, in particular up to 0.006% N, up to 0.012% S, in particular up to 0.006% S, 0.1 - 0.5% Ti, and 0.1 - 0.3% P and the remainder of iron and unavoidable Impurities is, wherein for the ratio% Ti /% P of Ti content% Ti to P content% P applies $$\mathrm{1}\mathrm{.}\mathrm{0}\mathrm{\le }\mathrm{\%}\mathrm{Ti}\mathrm{/}\mathrm{\%}\mathrm{P}\mathrm{\le }\mathrm{2}\mathrm{.}\mathrm{0th}$$

The invention uses FeTi phosphides (FeTiP) to increase the strength. Thus, according to the invention, a silicon steel with Si contents of 1.0-4.5% by weight, in practice, in particular of 2.4-3.4% by weight, is alloyed with titanium and phosphorus in order to obtain fine FeTiP. Form precipitates and increase the strength of NO electrical steel strip or sheet by particle hardening.

A particularly practical embodiment of the inventive alloy of an electrical strip or sheet is obtained when the contents of the steel of Si, C, N, S, Ti and P are each optionally (in wt .-%) to 2.4 - 3, 4% Si, up to 0.005% C, up to 0.006% N, up to 0.006% S, up to 0.5% Ti or up to 0.3% P. In addition, up to 2.0% Al and up to 1.0% Mn can be present in the steel according to the invention.

The invention uses to increase the strength instead of the carbonitrides usually used for FeTi phosphides. In this way, on the one hand the magnetic aging can be avoided, which can occur as a result of high C and / or N contents. In addition to the simultaneous presence of a sufficient absolute amount of Ti and P is crucial that the ratio of Ti content% Ti to P content% P satisfies the condition specified in claim 1, according to which the ratio of the titanium content to the phosphorus content of the electrical steel strip or sheet according to the invention is greater than or equal to 1.0 and at the same time less than or equal to 2.0. Only by adhering to the narrow windows of the contents of Ti and P and their content ratio, which are predetermined according to the invention, is it ensured that the electrical steel sheet or strip assembled in accordance with the invention has a sufficient number and sufficient distribution of FeTiP particles, in addition to sufficiently high strength also to ensure good electromagnetic properties. By adjusting the ratio% Ti to% P according to the invention, on the one hand, a harmful excess of phosphorus is avoided, which would lead to embrittlement in the electrical steel strip or sheet according to the invention. On the other hand, an excessive excess of titanium is avoided by the ratio predetermined according to the invention. Such an excess of Ti could lead to the formation of titanium nitrides, which would adversely affect the magnetic properties of the electrical steel strip or sheet.

The invention is based on the recognition that a maximum of the present invention used effect of the simultaneous presence of Ti and P is achieved in a non-grain oriented electrical sheet or strip according to the invention, if its contents of Ti and P with the smallest possible deviations of the stoichiometric ratio of 1.55. A consideration of this realization and at the same time for the practice Therefore, a particularly important embodiment of the invention provides that the ratio% Ti /% P of the Ti content% Ti to the P content% P applies $$\mathrm{1}\mathrm{.}\mathrm{43}\mathrm{\le }\mathrm{\%}\mathrm{Ti}\mathrm{/}\mathrm{\%}\mathrm{P}\mathrm{\le }\mathrm{1}\mathrm{.}\mathrm{67th}$$

The FeTiP particles made possible by the steel composition according to the invention regularly have a diameter which is much smaller than 0.1 μm. This takes into account the effect that although the strength of a material increases with the number of lattice defects, such as foreign atoms, dislocations, grain boundaries or particles of another phase, these lattice defects have a negative influence on the magnetic characteristics of a material. The negative influence is, as known per se, the strongest when the particle size is in the range of the Bloch wall thickness (transition region between magnetic domains with different magnetization), d. H. is about 0.1 microns. By significantly smaller particles used according to the invention for the increase in strength, this negative influence occurs in an electrical steel sheet according to the invention at most in a highly minimized form. Occasionally FeTiP particles may also be present in the material according to the invention which are significantly larger than 0.1 μm. However, these influence the properties of a product according to the invention at most to a negligible extent.

In an alloy composed according to the invention, those which are usually alloyed to increase the strength by forming carbonitrides Micro-alloying elements, such as Nb, Zr or V, are no longer needed in conjunction with high levels of carbon or nitrogen. Higher contents of C and N have a negative impact on the magnetic properties of the correspondingly assembled non-grain oriented electrical steel strip or sheet because they entail undesirable magnetic aging of the materials during practical use. According to the invention, therefore, the increase in strength is achieved by particle hardening, namely by the presence of FeTiP precipitates, but not with the help of carbon and / or nitrogen whose presence would lead to aging effects.

Accordingly, electrical tapes or sheets composed according to the present invention regularly have remagnetization losses P _{1.0 / 400} at a polarization of 1.0 Tesla and a frequency of 400 Hz at a thickness of the electrical steel or sheet of 0.5 mm of at most 65 W / kg and at a thickness of 0.35 mm at most 45 W / kg. At the same time, as compared with a conventionally composed alloy which does not have effective contents of Ti and P but otherwise has contents of the other alloying elements that are consistent with an alloy according to the invention, they regularly increase the yield strength of at least 60 MPa.

The inventive method is designed so that it enables the reliable production of a non-grain-oriented electrical tape or sheet according to the invention.

For this purpose, first of all a hot strip composed in the manner explained above for the non-grain-oriented electrical sheet or strip according to the invention is provided, which is subsequently cold-rolled and subjected to a final annealing as a cold-rolled strip. The final annealed cold-rolled strip obtained after the final annealing then represents the electrical strip or sheet assembled and obtained according to the invention.

The manufacture of the hot strip provided according to the invention can be carried out conventionally as far as possible. For this purpose, first of all a molten steel having a composition corresponding to the specification according to the invention (Si: 1.0-4.5%, Al: up to 2.0%, Mn: up to 1.0%, C: up to 0.01% , N: up to 0.01%, S: up to 0.012%, Ti: 0.1-0.5%, P: 0.1-0.3%, remainder iron and unavoidable impurities, data in% by weight. %, wherein for the ratio% Ti /% P of the Ti content% Ti to the P content% P is 1.0 ≤% Ti /% P ≤ 2.0) are melted and cast to a starting material, in which it in conventional manufacturing can be a slab or thin slab. However, since the precipitation formation processes according to the invention take place only after solidification, it is in principle also possible to cast the molten steel into a cast strip, which is then hot rolled into a hot strip.

The starting material thus produced can then be brought to a pre-material temperature of 1020-1300 ° C. For this purpose, the starting material is, if necessary, reheated or kept at the respective target temperature by utilizing the casting heat.

The thus heated starting material can then be hot rolled to a hot strip having a thickness which is typically 1.5-4 mm, in particular 2-3 mm. The hot rolling starts in a conventional manner at a hot rolling start temperature of 1000 - 1150 ° C and ends with a hot rolling end temperature of 700 - 920 ° C, in particular 780 - 850 ° C.

The resulting hot strip can then be cooled to a coiling temperature and coiled into a coil. The coiler temperature is ideally chosen so that precipitation of the Fe-Ti phosphides is avoided in order to avoid problems during subsequent cold rolling. In practice, the reel temperature for this purpose, for example, at most 700 ° C.

Optionally, the hot strip can be subjected to a hot strip annealing.

The supplied hot strip is cold rolled to a cold strip having a thickness typically in the range of 0.15-1.1 mm, especially 0.2-0.65 mm.

The final annealing contributes significantly to the formation of FeTiP particles used in the present invention for increasing the strength. By varying the annealing conditions of the final annealing, it is possible to optimize the material properties optionally in favor of a higher strength or a lower loss of core loss. Non-grain-oriented electrical sheets or tapes according to the invention having yield strengths of between 390 and 550 MPa and remagnetization losses P of _{1.0 / 400} , which are less than 27 W / kg at a strip thickness of 0.35 mm and a strip thickness of 0, 5 mm less than 47 W / kg, can be particularly reliable achieved in accordance with a first variant of the method according to the invention that the cold strip in the course of the final annealing completed in a continuous furnace two-stage Kurzzeitglühung in which the cold strip in the first annealing stage d.1) first annealed over an annealing period of 1 - 100 s at an annealing temperature of at least 900 ° C and at most 1150 ° C and then in a second annealing stage d.2) over an annealing period of 30 - 120 s at an annealing temperature of 500 - 850 ° C. , In this variant, the already existing FeTiP precipitates are dissolved in the first annealing stage d.1) and a complete recrystallization of the microstructure is achieved. In the second annealing stage d.2) then the targeted excretion of FeTiP particles.

In order to achieve a further improvement in the strength level of the non-grain-oriented electric sheet or strip obtained according to the above-explained two-stage short-time annealing, the long-term annealing optionally carried out in the hood furnace may be followed by the two-stage short-time annealing, in which the cold strip is baked at temperatures of 550-660 ° C over a Annealing time of 0.5 - 20 h is annealed. The achievable by this additional Langzeitglühung increase in yield strength is regularly at least 50 MPa.

Non-grain oriented electrical sheets or tapes having yield strengths of 500-800 MPa and remagnetization losses P _{1.0 / 400} of less than 45 W / kg for 0.35 mm thick electrical sheets or tapes can also be produced thereby according to a second variant of the method of the invention in that the final annealing is carried out as a short-time annealing, in which the cold strip is annealed in the continuous furnace for an annealing period of 20 to 250 seconds at an annealing temperature of 750 to 900 ° C. Due to the lower annealing temperature in this case no complete recrystallization of the microstructure is achieved. However, the desired strength-increasing FeTiP precipitates form.

An alternative possibility of producing non-grain-oriented electrical steel sheets according to the invention having yield strengths which are in the range of 500-800 MPa and magnetic reversal losses P _{1.0 / 400} of less than 45 W / kg for 0.35 mm thick electrical sheets or strips can be used according to US Pat a third variant of the method according to the invention are also obtained in that the final annealing is carried out as a long-term annealing in the hood furnace, in which the cold strip is annealed over a 0.5 - 20 h duration annealing at an annealing temperature of 600 - 850 ° C. In this variant, it does not come to a completely recrystallized structure. However, FeTiP precipitates are formed which are finer than the FeTiP precipitates present in the non-grain oriented electrical sheets or tapes of the invention produced in accordance with the first embodiment discussed above. It can be through the illustrated here third variant of the invention

Method in comparison to the above-explained second variant to achieve improvements in Ummagnetisierungsverluste.

Optionally, in the third variant of the process according to the invention after the long-term annealing, a short-time annealing in the continuous furnace can also be carried out, in which the respective cold-rolled strip is annealed at 750 ° C.-900 ° C. over an annealing period of 20-250 seconds. This additional Kurzzeitglühung can improve the degree of recrystallization of the structure. Along with this, an improvement in the loss of magnetization is to be expected.

In order to introduce a critical energy by increasing the dislocation density, so that the recrystallization is initiated in the subsequent Kurzzeitglühung, the cold strip in the course of the third variant of the inventive method between the long-term annealing and the Kurzzeitglühung optionally a deformation with a degree of deformation of at least 0.5 % and at most 12%. Such a forming step, which is usually carried out as an additional cold-rolling step, furthermore contributes to the improvement of the flatness of the non-grain-oriented electrical sheet or strip obtained at the end of this process variant according to the invention. The effects achieved with the optionally additionally carried out cold deformation can be achieved particularly reliably if the degrees of deformation of the cold deformation amount to 1 to 8%.

The final annealing may be followed by a smoothing pass carried out in a conventional manner.

Furthermore, the obtained, non-grain oriented electrical steel strip or sheet material may be finally subjected to a conventional flash annealing. Depending on the processing operations at the end processor, this flash annealing can still be performed in the coil of the manufacturer of NO-electric strip or sheet according to the invention, or it can first be divided from the produced in the inventive manner electrical strip or sheet, the blanks processed at the final processor, then the Be subjected to flash annealing.

The invention of embodiments will be explained in more detail.

The experiments described below were carried out under laboratory conditions. Here, first of all, a molten steel TiP and a reference melt Ref according to the invention have been melted and cast into slabs. The compositions of the melt TiP and Ref are given in Table 1. With the exception of their lacking effective contents of Ti and P, not only the alloying elements in the reference melt ref, but also their contents in accordance with the usual tolerances agree with the melt TiP according to the invention.

The slabs were brought to 1250 ° C temperature and with a hot rolling start temperature of 1020 ° C and a hot rolling end temperature of 840 ° C to hot-rolled into a 2 mm thick hot strip. The respective hot strip has been cooled to a _reel temperature T _reel . Subsequently, a typical cooling in the coil has been simulated.

Three samples of the hot strip consisting of the steel alloy TiP according to the invention and a sample of hot strips made of the reference steel Ref were then subjected to a hot strip annealing at a temperature of 740 ° C. for a period of 2 hours and then to a cold strip with a final thickness of 0, 5 mm or 0.35 mm cold rolled.

On the other hand, two further samples of the hot strips consisting of the steel alloy TiP according to the invention and a further sample of the hot strips consisting of the reference steel Ref have been cold rolled into a 0.5 mm thick cold strip without annealing.

This was followed by a two-stage final annealing. In the first annealing stage, the samples were heated to 1100 ° C and held there for 15 seconds, so that the Ti and P contained in them was mostly in solution. This was followed by the second annealing step, in which annealing was carried out at a temperature T _low which is clearly below the excretion temperature T _Aus of FeTiP. In this way, the desired fine, a mean 0.01 - 0.1 micron FeTi phosphide precipitates formed.

In Table 2, for the samples cold-rolled to a thickness of 0.5 mm and in Table 3 for the Thickness of 0.35 mm cold-rolled specimens indicated respectively the _reel temperature T _reel and the temperature T _low . In addition, the sample for each of the samples, the upper yield point R _eH, the lower yield point R _eL, the tensile strength R _m which respectively determined at 50 Hz core losses P are shown in Tables 2 and 3, in each case measured in the transverse and the longitudinal direction of _1.0 ( Loss of magnetization at a polarization of 1.0 T), P _1.5 (loss of magnetization loss at a polarization of 1.5 T) and the polarization J ₂₅₀₀ (polarization at a magnetic field strength of 2500 A / m) and J5000 (polarization at a magnetic Field strength of 5000 A / m), as well as at a frequency of 400 Hz or 1 kHz respectively determined Ummagnetisierungsverluste P _1.0 (loss of magnetization at a polarization of 1.0 T) indicated.

It can be seen that the lower yield strength R _eL in the samples composed and processed _according to the invention is _60-100 MPa higher in comparison with the samples produced from the reference steel Ref. By contrast, there is no significant difference between the samples produced with and without hot-band annealing. Also, a variation of the reel temperature or the temperature T _low has no significant influence on the mechanical properties.

At a frequency of 50 Hz, the samples produced from the steel according to the invention have somewhat of 3.9-4.8 W / kg for 0.5 mm thick sheets and less than 3.7 W / kg for 0.35 mm thick sheets higher Ummagnetisierungsverluste P _1.5 than that from the Reference steel produced samples. Again, the reel temperature has no significant influence.

In contrast, at higher frequencies of 400 Hz and 1 kHz, the magnetic reversal losses P _1.0 for the invention and the reference samples are very close to each other. The samples with the higher temperature T _low of 700 ° C show here in the case of 0.5 mm thick sheets with less than 39 W / kg at 400 Hz and less than 180 W / kg at 1 kHz lower Ummagnetisierungsverluste P _1.0 than the reference material. In the case of the 0.35 mm thick sheets, the same loss of magnetization is achieved as with the reference material.

In another series of experiments, a steel TiP2 has been melted and cast into slabs whose composition is given in Table 4. The ratio% Ti /% P of the Ti content% Ti to the P content% P in the steel is TiP2% Ti /% P = 1.51.

The slabs were reheated to 1250 ° C and then hot rolled to hot strip with a hot strip thickness of 2.1 mm and 2.4 mm, respectively. The hot rolling start temperature was in each case 1020 ° C., while the hot rolling end temperature was in each case 840 ° C. The resulting hot strips were then reeled at a reel temperature of 620 ° C.

Subsequently, the hot strips thus obtained were cold rolled without prior hot strip annealing to 0.35 mm thick cold strip.

Samples of the cold strips thus obtained have been subjected to different variants of final annealing.

In the first variant, a two-stage Kurzzeitglühung has been completed in a continuous furnace. In the first stage of the Kurzzeitglühung each specified in Table 5 annealing times t _{G1 are} met and there also mentioned respective maximum annealing temperatures T _max1 achieved while the second stage respectively in the annealing times t _G2 also shown in Table 5 at the same there maximum annealing temperatures T _{max2 has been} completed. The mechanical and magnetic properties determined on the thus obtained final annealed NO-electric sheet samples in transverse direction Q and longitudinal direction L are also listed in Table 5.

A sample of the finally heat-treated samples according to the first variant has subsequently been subjected to additional long-term annealing in a hood furnace. The annealing times t _GH and maximum annealing temperatures T _maxH are shown in Table 6. The mechanical and magnetic properties determined on the additionally long-time annealed NO electric sheet in the transverse direction Q and in the longitudinal direction L are likewise recorded in Table 6. It can be seen that the supplementary long-term annealing achieved a significant increase in the yield strength R _e and the tensile strength R _m , whereas the magnetic properties did not deteriorate significantly.

In a second variant of the final annealing, samples of the cold strips have been subjected to long-term annealing at different temperatures T _maxH in the hood furnace over an annealing time t _GH . The respective temperatures T _maxH and the respective annealing time t _GH are listed in Table 7. Table 7 also shows the mechanical and magnetic properties determined on the long-time-annealed NO-electric sheet samples obtained in the transverse direction Q and in the longitudinal direction L.

In a third variant of the final annealing, samples of the cold strips have been subjected to single-stage short-time annealing at different temperatures T _maxD in the continuous furnace over an annealing time t _GD . The respective temperatures T _maxD and the respective annealing time t _GD are listed in Table 8. Table 8 also shows the mechanical and magnetic properties determined on the long-time-annealed NO electric-sheet samples obtained in the transverse direction Q and in the longitudinal direction L.

The invention accordingly relates to a non-grain-oriented electrical steel sheet or sheet comprising, in addition to iron and unavoidable impurities (in% by weight) Si: 1.0-4.5%, Al: up to 2.0%, Mn: up to 1.0%, C: up to 0.01%, N: up to 0.01%, S: up to 0.012%, Ti: 0.1-0.5%, P: 0.1-0 , 3%, wherein the ratio% Ti /% P of the Ti content% Ti to the P content% P is 1.0 ≤% Ti /% P ≤ 2.0. An inventive non-grain oriented electrical steel strip or sheet and made of such a sheet or strip components for electrical applications are characterized by increased Strengths and at the same time good magnetic properties. The NO sheet or strip according to the invention can be produced by cold-rolling a hot strip consisting of a steel with the above-mentioned composition into a cold strip and subjecting this cold strip to a final annealing. For special expression of certain properties of the NO-band or sheet, the invention provides various variants of this final annealing available. Table 1 variants Si al Mn C N S Ti P TiP 2, 99 0,004 0.58 0,006 0.0021 <0.001 0.148 0,100 Ref 2.96 0,006 0, 64 0,006 0.0021 0.001 0.001 0,004 Residual iron and unavoidable impurities,
Data in% by weight stole According to the invention? Hot strip annealing? samples direction T _reel T _low R _eH R _eL R _m 50 Hz 400Hz 1kHz P _1.0 P _1.5 J ₂₅₀₀ J ₅₀₀₀ P _1.0 P _1.0 [° C] [° C] [MPa] [MPa] [MPa] [W / kg] [W / kg] [T] [T] [W / kg] [W / kg] TiP YES YES L 310 550 409 403 573 2.01 4.47 1.59 1.68 44.4 197 Q 430 426 593 2.20 4.76 1.57 1, 66 46.8 213 YES L 620 550 403 396 560 2.08 4.43 1.57 1.67 43.3 199 Q 421 418 582 1.97 4.44 1.55 1.65 40.3 181 YES L 620 700 400 395 554 1.76 3.93 1.58 1.67 36.4 164 Q 431 424 589 1.86 4, 17 1.55 1, 64 38.9 178 Ref NO YES L 620 - 329 321 472 1.72 3.78 1, 61 1.70 43.9 205 Q 351 340 492 1.63 3.88 1.53 1.63 43.4 207 TiP YES NO L 310 550 407 402 572 2.16 4.50 1.57 1.66 45, 1 209 Q 433 429 591 1.98 4.59 1.54 1.64 40.2 181 NO L 620 550 402 396 564 2.23 4, 65 1.57 1, 66 46.4 214 Q 426 423 586 2.19 4.77 1.53 1.63 46.2 214 Ref NO NO L 620 - 365 339 480 1.47 3.34 1.63 1.71 38, 0 173 Q 382 362 500 1.55 3, 68 1.53 1.63 40.4 191 stole According to the invention? Hot strip annealing? samples direction T _reel T _low R _eH R _eL R _m 50 Hz 400Hz 1kHz P _1.0 P _1.5 J ₂₅₀₀ J ₅₀₀₀ P _1.0 P _1.0 [° C] [° C] [MPa] [MPa] [MPa] [W / kg] [W / kg] [T] [T] [W / kg] [W / kg] TiP YES NO L 620 700 430 415 579 1.77 3.74 1.55 1.65 26.4 112 Q 456 442 603 1.62 3.71 1.52 1.62 23.0 94 Ref NO NO L 620 - 350 331 466 1.26 3.06 1.57 1.66 23.6 100 Q 359 344 453 1.28 3.22 1.54 1.63 23.2 99 variant Si al Mn C N S Ti P tip2 3.05 0.689 0, 155 0.0036 0.0021 0.0008 0, 173 0.115 Residual iron and unavoidable impurities,
Data in% by weight T _max1 t _G1 T _max2 t _G2 samples direction R _eH R _el or R _p0.2 rm 50 Hz 400 Hz 1 kHz P _1.0 P _1.5 J ₂₅₀₀ J ₅₀₀₀ P _1.0 P _1.0 [° C] [s] [° C] [s] [MPa] [MPa] [MPa] [W / kg] [W / kg] [T] [T] [W / kg] [W / kg] 1070 55 700 50 L 448 442 608 1.60 3.9 1.54 1.63 20.5 79 Q 474 471 636 2.24 4.81 1.49 1, 58 25.3 92 1100 40 700 50 L 439 582 1.25 3.13 1.54 1.63 18.5 76 Q 468 600 1.77 3.87 1.48 1.58 22.9 88 T _maxH t _GH samples direction R _eH R _el or R _p0.2 rm 50 Hz 400 Hz 1 kHz P _1.0 P _1.5 J ₂₅₀₀ J ₅₀₀₀ P _1.0 P _1.0 [° C] [H] [MPa] [MPa] [MPa] [W / kg] [W / kg] [T] [T] [W / kg] [W / kg] 620 5 L 484 478 640 1.68 4.03 1.55 1.65 22.2 86 Q 513 511 654 2.24 4, 91 1.5 1.6 26.6 99 T _maxH t _GH samples direction R _eH R _el or R _p0.2 rm 50 Hz 400 Hz 1 kHz P _1.0 P _1.5 J ₂₅₀₀ J ₅₀₀₀ P _1.0 P _1.0 [° C] [H] [MPa] [MPa] [MPa] [W / kg] [W / kg] [T] [T] [W / kg] [W / kg] 620 5 L 753 724 866 3.83 8.4 1.52 1.62 39.1 128 Q 814 801 919 4.35 9.45 1.44 1.55 43.6 - 700 5 L 666 615 781 3.43 7, 62 1.54 1.63 36.3 121 Q 705 668 823 3.87 8.51 1.45 1.55 39.3 131 740 5 L 614 567 739 3.39 7, 63 1.54 1, 64 36.2 123 Q 657 609 777 3.86 8, 65 1.47 1.58 40 136 840 5 L 560 524 686 3.62 7, 96 1.55 1.65 38.5 128 Q 602 560 712 3, 97 8, 61 1.5 1.6 42.0 - T _{maxD GD} samples direction R _eH R _el or R _p0.2 rm 50 Hz 400 Hz 1 kHz P _1.0 P _1.5 J ₂₅₀₀ J ₅₀₀₀ P _1.0 P _1.0 [° C] [s] [MPa] [MPa] [MPa] [W / kg] [W / kg] [T] [T] [W / kg] [W / kg] 900 60 L 585 541 713 4.06 8.62 1.54 1.63 42.1 143 Q 627 589 770 4.38 9.36 1.47 1.57 43.8 145 800 80 L 630 606 790 4.06 8.69 1.52 1.61 41.7 140 Q 672 667 843 4.39 9.5 1.45 1.55 43.8 142 700 150 L - 735 878 4.5 9.68 1.51 1.61 44, 9 145 Q - 832 926 5.09 10.98 1.43 1.54 48.7 154

Claims (15)

Non-oriented electrical steel strip or sheet for electrotechnical applications made of a steel containing, in addition to iron and unavoidable impurities (in% by weight)
Si: 1.0 - 4.5%,
Al: up to 2.0%,
Mn: up to 1.0%,
C: up to 0.01%,
N: up to 0.01%,
S: up to 0.012%,
Ti: 0.1-0.5%,
P: 0.1 - 0.3%
wherein the ratio% Ti /% P of the Ti content% Ti to the P content% P applies $$\mathrm{1}\mathrm{.}\mathrm{0}\mathrm{\le }\mathrm{\%}\mathrm{Ti}\mathrm{/}\mathrm{\%}\mathrm{P}\mathrm{\le }\mathrm{2}\mathrm{.}\mathrm{0th}$$

Non-oriented electrical steel strip or sheet according to claim 1, characterized in that for the ratio% Ti /% P of the Ti content% Ti to the P content% P applies $$\mathrm{1}\mathrm{.}\mathrm{43}\mathrm{\le }\mathrm{\%}\mathrm{Ti}\mathrm{/}\mathrm{\%}\mathrm{P}\mathrm{\le }\mathrm{1}\mathrm{.}\mathrm{67th}$$

Non-grain-oriented electrical steel strip or sheet according to one of the preceding claims, characterized in that its Si content is 2.4-3.4% by weight. Non-grain oriented electrical steel strip or sheet according to any one of the preceding claims, characterized in that its C content is at most 0.006 wt .-%. Non-grain oriented electrical steel strip or sheet according to any one of the preceding claims, characterized in that its N content is at most 0.006 wt .-%. Non-oriented electrical steel strip or sheet according to any one of the preceding claims, characterized in that its S content is at most 0.006 wt .-%. Non-oriented electrical steel strip or sheet according to one of the preceding claims, characterized in that its core loss P _{1.0 / 400} at a polarization of 1.0 Tesla and a frequency of 400 Hz at a thickness of the electrical strip or sheet of 0.5 at most 65 W / kg and at a thickness of 0.35 mm at most 45 W / kg. Component for electrotechnical applications, produced from a manufactured according to one of claims 1 to 7 electrical steel or sheet. Method for producing a non-grain-oriented electrical strip or sheet, in which the following work steps are performed: a) providing a hot strip consisting of a steel containing in addition to iron and unavoidable impurities (in% by weight)
Si: 1.0 - 4.5%,
Al: up to 2.0%,
Mn: up to 1.0%,
C: up to 0.01%,
N: up to 0.01%,
S: up to 0.012%,
Ti: 0.1-0.5%,
P: 0.1 - 0.3%
wherein the ratio% Ti /% P of the Ti content% Ti to the P content% P applies $$\mathrm{1}\mathrm{.}\mathrm{0}\mathrm{\le }\mathrm{\%}\mathrm{Ti}\mathrm{/}\mathrm{\%}\mathrm{P}\mathrm{\le }\mathrm{2}\mathrm{.}\mathrm{0};$$

b) cold rolling the hot strip to a cold strip and c) Final annealing of the cold strip. A method according to claim 9, characterized in that the cold strip completed during the final annealing in a continuous furnace two-stage short-time annealing passes through, where the cold strip d.1) initially in a first annealing stage over an annealing period of 1 - 100 s at an annealing temperature of at least 900 ° C and at most 1150 ° C and then d.2) is annealed in a second annealing stage over an annealing period of 30 - 120 s at an annealing temperature of 500 - 850 ° C. A method according to claim 10, characterized in that the cold strip is subjected after the second stage of the Kurzzeitglühung over a annealing period of 0.5 - 20 h extending long term annealing at an annealing temperature of 550 - 660 ° C in a hood furnace. A method according to claim 9, characterized in that the final annealing of the cold strip is carried out as Kurzzeitglühung at which the cold strip is annealed in a continuous furnace for 20 - 250 sec at an annealing temperature of 750 - 900 ° C. A method according to claim 9, characterized in that the final annealing is carried out as a long-term annealing, in which the cold strip in the hood furnace via a Annealing for 0.5 to 20 hours is annealed at an annealing temperature of 600 to 850 ° C. Process according to claim 13, characterized in that the final annealing additionally comprises a short-time annealing carried out after long-term annealing, in which the cold strip passes through a continuous furnace over an annealing period of 20 to 250 sec at an annealing temperature of 750 to 900 ° C. A method according to claim 14, characterized in that the cold strip is subjected between the long-term annealing and the Kurzzeitglühung a deformation with a degree of deformation of at least 0.5% and at most 12%.