ࡱ> hj5@ ;bjbj22 4^XXOI9998:9L;.n6<>"??0?MMM)++++++$RHOUKMUUO?0? rrrU?(0?)rU)rJr&srE}TJE~0?*< Ћ^#b9kb},0.}6ppP6E~6E~MO:rPQKMMMOO+/d r/The origin of the surface field enhanced coercive field in nanophase Fe73.5Cu1Nb3Si15.5B7 ribbon Stjepan Sabolek, Emil Babi, Ivica Kuaevi, Marko `uaak, Dario Posedel and Denis Stani Department of Physics, Faculty of Science, University of Zagreb, Bijeni ka 32, 10000 Zagreb, Croatia Corresponding author: Stjepan Sabolek Department of Physics Faculty of Science, University of Zagreb Bijeni ka 32 10000 Zagreb, Croatia Tel: +385 1 460 5555 fax: +385 1 468 0336 E-mail address: sabolek@phy.hr Abstract The influence of surface fields Hp (generated with either direct or alternating core-current) on soft magnetic properties of amorphous and nanocrystalline Fe73.5Cu1Nb3Si15.5B7 ribbon has been studied. While in amorphous ribbon the coercive field Hc decreases with Hp, in the same optimally annealed ribbon (Hc = 1.3 A/m, Mm ( Ms) Hc increases with Hp and the hysteresis loss E decreases with Hp for all explored types of Hp (static and dynamic with different phases in respect to that of the magnetizing field H). The unexpected increase of Hc in nanocrystalline ribbon is associated to the influence of Hp on the surface and main (inner) domain structure. The model is developed which takes into account this interaction and explains all the experimental results. The probable adverse effect of the external fields with configurations similar to those of Hp on the performance of such ribbons is briefly discussed and some procedures which can prevent these effects are proposed. PACS classification codes: 75.50.Kj; 75.60.Ch Keywords: Hysteresis loop; Domain structure; Domain wall pinning; Coercive field; Core current Introduction The core-currents strongly affect the M-H loops and hysteresis loss (E) of amorphous ferromagnetic ribbons (1, 2(. In particular, the direct current (JD) may decrease the coercive field Hc (hence decrease of E), shift the center of the M-H loop (C) along the H-axis, and change the permeability, maximum (Mm) and remanent (Mr) magnetization of the sample (3(. Detailed investigations have shown that these effects are associated with perpendicular field Hp generated by JD (static Hp). The magnitude of Hp increases linearly with the distance y from the center of the ribbon (y = 0) and reaches the maximum at the surface of the sample (Hp = JDy/w, where w is the ribbon width and t/2 ( y ( t/2 is the perpendicular distance from the center of the sample with t ribbon thickness (2(), hence the term surface field. Similar effects caused by the surface field Hp generated from external sources (4( prove that Hp and not the core-current itself causes the observed effects. Later on it was found that Hp generated by alternating core-current JA (dynamic Hp) decreases more efficiently Hc than static Hp (5(. In order to explain the observed effects and to help the understanding of the magnetization processes in soft ferromagnetic ribbons a simple model for the influence of surface fields Hp on the magnetization of the sample consisting of two domains with antiparallel domain magnetization (I) has been developed (6(. This model in addition to the explanation of the changes in the M-H loop caused by Hp also provides a qualitative (sometimes quantitative) insight into the domain wall (DW) pinning, domain structure and the magnetic anisotropy. For the coercive field model predicts a linear decrease of Hc with Hp (at not too small Hp) providing that I forms an angle with the ribbon axis. The measurements of Hc vs. Hp for a number of amorphous ferromagnetic ribbons (both magnetostrictive and nonmagnetostrictive) agreed well with the model prediction for moderate values of static Hp, whereas at elevated Hps the decrease of Hc with Hp slows down and Hc tends to saturation (3(. The effects of dynamic Hp on Hc were qualitatively the same as for static Hp, but in several samples (in which the difference in DW pinning strengths at opposite surfaces was sufficiently large) the decrease of Hc with increasing Hp continued until Hc = 0 was reached (5(. The observed deviations from the model predictions at elevated Hps were ascribed to the complex domain structure of real sample and the influence of high surface field on this structure, but these ingredients have not been incorporated in the model. However, recent measurements show [7] that Hc of the nanocrystalline Fe73.5Cu1Nb3Si15.5B7 ribbon (thereafter FeCuNbSiB) increases with Hp (whereas loss E decreases with Hp) which is at variance with the predictions of simple model for the influence of Hp on the M-H loops of ferromagnetic ribbons. These results call for the revision of the model which should take into account the influence of the surface field on the actual domain structure (DS) and the DW pinning associated with the surface DS (SDS). Here, we in addition to the description of the 'unusual' influence of Hp (both static and dynamic) on the M-H loops and their parameters for nanocrystalline FeCuNbSiB ribbon also present the improved model which fully accounts for the observed phenomena. This model yields a better insight into the magnetization processes in the soft ferromagnetic ribbons and may also help to find the methods for the improvement of their soft magnetic properties. Experimental procedures The amorphous FeCuNbSiB ribbon with dimensions l ( w ( t = 200 ( 2 ( 0.02 mm3 was prepared by the melt-spinning technique in Vacuumschmelze GmbH, Hanau, Germany. After the magnetization measurements of the as prepared sample the same ribbon was brought into the nanocrystalline state by thermal annealing at Ta = 540(C for one hour. The annealing was performed in a long tube furnace in the atmosphere of pure argon gas. The magnetization measurements were performed with an induction technique at room temperature (8(. In all magnetization measurements we used triangular magnetizing field H(t) with the frequency f = 5.5 Hz. For the measurement of Hc and Mr as a function of Mm/Ms (Ms is the saturation magnetization) we varied the amplitude H0 of the magnetizing field (H0 ( 350 A/m). The investigation of the influence of the static and dynamic Hp on the M-H loops and their parameters (Hc, C, Mm, Mr, (max) was performed at fixed amplitudes of H (H0 = 100 A/m and 10 A/m). The static and dynamic surface fields Hp were achieved with either direct (JD ( 100 mA) or alternating current (JA = JA0sin(t with JA0 ( 110 mA and ( = 2(f = 11(/s) flowing along the ribbon. The magnetizing field H and the alternating core-current JA were synchronized with the phase of JA shifted for either (/2 (inset to Fig.1) or 3(/2 in respect to that of H. Some data relevant to our FeCuNbSiB sample (both for amorphous and nanocrystalline state) are given in Table 1. The model The model we propose is based on the following common characteristics of the soft ferromagnetic samples in the shape of long ribbon: The domain structure has usually two components: the main (inner) domain structure (MDS) which consists of rather wide domains separated with 180(-DWs and dominates the magnetization of the ribbon along its axis [9], and the surface domain structure (SDS) consisting of fine domains forming a complex patterns associated with the closure of the magnetizations of MDS, local magnetic anisotropy and the surface inhomogeneities [10]; The magnetizations of the domains I of the MDS form nonzero angle ( with the ribbon axis and this angle is not the same for all domains of MDS [11]; Because of usually small angles ( the magnetization of the ribbons in moderate fields along the axis (such as those used in present measurements) proceeds usually via the motion of 180(-DWs of MDS [12, 13]; Usually the strongest pinning centres for DWs of MDS are located in the vicinity of the surfaces of the sample and their strengths are usually different at the opposite surfaces[14]; These surface pinning centres are associated with the surface inhomogeneities, stresses and irregularities/roughness (intrinsic pinning), and also with some domains from SDS whose magnetizations form large angles ( with the ribbon axis (SDS pinning) [15]. For simplicity we consider the motion of one 180(-DW separating two domains from MDS with antiparallel Is (Fig. 1.). In order to account for more complex MDS of real ribbon we denote the angle between the domain magnetizations and ribbon axis with <(>, which could be regarded as an average value of ( corresponding to MDS domains participating in the magnetization processes for given magnetizing field amplitude H0. The magnitudes of H necessary for depinning of DWs at the upper and lower surface of the ribbon (in the absence of the surface field Hp) we denote as Hsu0 and Hsl0 respectively (subscript 0 denotes Hp = 0). Since usually Hsu0 ( Hsl0 we assume Hsu0 < Hsl0 [14]. Therefore, in the absence of Hp, Hc = Hsu0 ( Hc0. When JD flows along the sample during the magnetization cycle, the generated surface field Hp (Fig. 1) has the projection P = Hpsin<(> on I, which together with the projection of the magnetizing field Hcos<(> contributes to the pressure on DW. Accordingly, the magnitude of the magnetizing field H necessary for depinning of DW at the upper or lower surface of the ribbon may increase or decrease in respect to Hsu0 or Hsl0 depending on the direction of JD. (This was the essence of the earlier model which ignored SDS [6].) However, in a real sample there is an interplay between MDS and SDS and this interaction is affected by the surface field. In particular, the surface domains, which form large angles with the ribbon axis, can act as the pinning centres for DWs of MDS [15]. Clearly, this SDS type of DW pinning is enhanced with Hp which tends to fix and/or rotate the magnetizations of such domains. Therefore, the magnitude of the magnetizing field H necessary for depinning of DWs belonging to MDS will be enhanced and this enhancement will depend on the magnitude of Hp. This enhancement can be different at the opposite surfaces of the sample and its actual dependence on Hp is not known to us. However, in a case of moderate Hp it is reasonable to assume a linear variation of the SDS pinning with Hp. Therefore, we assume (and the experimental results for FeCuNbSiB ribbon seem to confirm) that the DW pinning enhancement due to SDS is equal for upper and lower surface of the ribbon respectively and is proportional to Hp i. e. kHp (where k is the proportionality constant which depends on the SDS of the given sample). Since we wish to model the dynamic M-H loops, we denote the magnitudes of the magnetizing field necessary for the depinning of DW belonging to MDS at the upper and lower surface of the sample in the presence of JD with Hsu and Hsl respectively when the magnetizing field increases from H0 to H0 and the corresponding symbols for the reverse part of the cycle (from H0 to H0) are  EMBED Equation.3  and  EMBED Equation.3 . Accordingly, the expressions for the depinning fields in the presence of JD are:  EMBED Equation.3  (1)  EMBED Equation.3  (2)  EMBED Equation.3  (3)  EMBED Equation.3  (4) The upper signs in eqs. (1) - (4) correspond to JD direction as shown in Fig. 1, whereas the lower signs correspond to the opposite direction of JD. Since the magnetization of the sample changes as soon as the magnetizing field H reaches the lower value of the two values necessary for the depinning of DW from the upper and lower surface of the sample, in a given conditions only a part of eqs. (1) - (4) will be relevant for the determination of the width (Hc) and the position of the center (C) of the M-H loop. Accordingly, when the strength of pinning of DWs at the opposite surface of the ribbon is different one has two different situations depending on EMBED Equation.3 . In a case A) when  EMBED Equation.3 , (Hsu(<(Hsl( and ( EMBED Equation.3 (<( EMBED Equation.3 ( is fulfiled for both directions of JD one finds:  EMBED Equation.3  (5) and  EMBED Equation.3 . (6) Acorrding to eqs. (5) and (6) the coercive field increases with Hp when SDS pinning is present, whereas the center C of the M-H loop shifts with Hp in either negative or positive direction along the H-axis, depending on the direction of JD. The shift C depends on angle <(> but not on SDS pinning since kHp terms cancel in eq. (6). For  EMBED Equation.3 , regime B, is (Hsu(<(Hsl( and ( EMBED Equation.3 (<( EMBED Equation.3 ( for the direction of JD as in Fig. 1, whereas for the opposite direction of JD (Hsl(<(Hsu( i ( EMBED Equation.3 (<( EMBED Equation.3 ( is fulfilled. The calculations analogous to those performed in a case A yield for both directions of JD:  EMBED Equation.3  (7) and  EMBED Equation.3 . (8) In this range of Hp the coercive field (eq. (7)) may either increase or decrease with Hp depending on k > or < tan <(> i.e. whether the enhancement of SDS pinning or a pressure of Hp on DWs prevails. In a special case k = tan <(>, Hc would remain constant at the magnitude reached at the end of regime A (eq. (5)). The position of the center of the M-H loop should be fixed (eq. (8)) at the maximum value reached in regime A (eq. (6)), providing that the enhancement of the SDS pinning at both surfaces of the sample is the same. Next we briefly describe the influence of dynamic Hp with the amplitude Hp0 on Hc and C. The calculation is simplified [5] by assuming that the alternating core current JA has the square wave form and the same frequency as H, but with phase adjusted in respect of that for H as illustrated in the inset to Fig. 1 (synchronization suitable for the decrease of Hc, hence suitable phase). In that case one obtains the relations for the depinning fields Hsi (i = u, l) from eqs. (1) (4) by taking into account the change in the direction of JA during the magnetization cycle (JA has opposite directions for the increasing (H0 ( H0) and decreasing (H0 ( -H0) branch of the M-H loop respectively):  EMBED Equation.3  (9)  EMBED Equation.3  (10)  EMBED Equation.3  (11)  EMBED Equation.3  . (12) Eqs. (9) (12) show that (Hsu(<(Hsl( and ( EMBED Equation.3 (<( EMBED Equation.3 ( irrespective of the amplitude of the surface field Hp0. Accordingly:  EMBED Equation.3  (13) should be fulfilled for any value of Hp0. The variation of Hc with Hp0 depends on k > or < tan <(> similarly to the case described by eq. (7). The center of the M-H loop is unshifted (C = 0, eqs. (9) and (11)). Further shift of the phase of JA in respect to that of H for additional 180( (unsuitable phase, causes an increase of Hc with Hp0 [6]) leads to the expressions for the depinning fields Hsi which are formally the same as eqs. (9) (12) but have opposite signs in front of Hp0tan<(> terms. However, in this case depending on the magnitude of Hp0 two regimes (analogous to those in the case of JD) with different variations of Hc appear: A) for  EMBED Equation.3  follows (Hsu(<(Hsl( and ( EMBED Equation.3 (<( EMBED Equation.3 ( with  EMBED Equation.3 , (14) which means that Hc increases with Hp0 irrespective of k > or < tan <(>, i.e. the broadening of M-H loop with Hp0 is further enhanced by the SDS pinning; B) for  EMBED Equation.3 , (Hsu(<(Hsl( and ( EMBED Equation.3 (<( EMBED Equation.3 ( is fulfilled, hence:  EMBED Equation.3 , (15) i.e. the variation of Hc with Hp0 depends on k > or < tan <(> as was the case in eq. (7). In both regimes the position of the center of the M-H loop does not depend on Hp0 i.e. C = 0 is fulfilled. The above expresions are derived for the square wave form of Hp0 (JA) whereas in the experiments we used sinusoidal JA. However, the earlier experiments have shown that the effect of sinusoidal Hp is practically the same as that of square wave one [5] and the sinusoidal JA results in less noise in the magnetization measurements. Although the above model for the influence of Hp on the SDS pinning of DWs belonging to MDS is quite general, in the derivation of specific results for Hc and C we used two simplifyng assumptions: the enhancement of SDS pinning is proportional to Hp (kHp or kHp0); this enhancement is the same at both surfaces of the sample (ku = kl ( k). The validity of these assumptions has to be verified by the experiment. Results and discussion The amorphous FeCuNbSiB ribbons show poor soft magnetic properties due to very strong local magnetic anisotropy (induced during the production of this magnetostrictive ferromagnet) and associated strong volume pinning centers for DWs [16]. Our measurements performed prior to thermal annealing confirm these findings (Table 1). Due to strong volume pinning of DWs belonging to MDS for H0 = 100 A/m the coercive field is quite large (13.5 A/m) and the ratio Mm/Ms quite small (0.4). The slope of logHc vs. log(Mm/Ms) variation (Fig. 2) is approximately constant within the explored range of Mm (Mm/Ms ( 0.5 for H0 ( 350 A/m). Since the strength of DW pinning is proportional to this slope [17] the unique slope indicates that one type of pinning centers dominates the magnetization processes in amorphous FeCuNbSiB ribbons for Mm/Ms ( 0.5. Simultaneously, the remanent magnetization tends to saturate for Mm/Ms > 0.3 (Fig. 2b). This is consistent with strong volume pinning which inhibits the motion of DWs (since Mm/Ms ( 0.5 only a fraction ( 50 % of MDS participates in the magnetization of the sample along its axis) and the magnetization processes for Mm/Ms > 0.3 possibly proceed via bulging of the free parts of DWs situated between strong pinning centres [17]. Since DW bulging is reversible process Mr saturates. Under such conditions the influence of static surface field on the parameters of the M-H loops is weak. Indeed, for H0 = 100 A/m Hc decreases approximately linearly with Hp (Fig. 3) for Hp ( 5 A/m in agreement with eq. (7) for k ( tan((( but the relative decrease is quite small ((Hc/Hc0 ( 0.1 for Hp = 24 A/m) and the changes of Mm and C with Hp are slight. This occurs because Hp has the largest magnitude at the surfaces of the sample (Hp = JD/2w) and therefore exerts little influence on strong volume pinning centers (located in the interior of the sample where Hp ( 0). Accordingly, the intrinsic surface pinning and SDS pinning have little influence on magnetization processes in as-prepared amorphous FeCuNbSiB ribbons. In order to check whether this conclusion depends on the magnitude of H0 (hence the value of Mm) or not, we also measured the influence of static Hp on the parameters of the M-H loop for H0 = 25 A/m (Mm ( 0.26Ms). As seen from Fig. 4, the variations of Hc, Mm and C with Hp for H0 = 25 A/m are essentially the same as those for H0 = 100 A/m (Fig. 3). In particular, for (Hp(( 5 A/m Hc decreases a little with Hp ((Hc/Hc0 ( 0.09 for Hp = 24 A/m) whereas the changes of Mm and C with Hp are slight (Fig. 4). Accordingly, throughout the explored range of H0 (hence also Mm) the surface pinning of DWs has little influence on the magnetization processes in amorphous FeCuNbSiB ribbons. After 1 hour annealing at Ta = 540(C, fine structure of nanocrystalline Fe3Si grains with diameters 10 15 nm forms within the residual amorphous phase [18, 19]. At that stage, the magnetocrystalline anisotropy is overcome by the exchange interaction between Fe3Si grains and the magnetoelastic anisotropy vanishes due to cancellation of the negative magnetostriction of the grains and positive magnetostriction of the amorphous phase [18, 19] (the sample becomes nonmagnetostrictive). This results in excellent soft magnetic properties of the annealed sample (Fig. 5a). In particular, a drastic reduction of the coercive field, large increase of Mm and large (max (Hc = 1.3 A/m, Mm/Ms ( 1 and (max ( 105 Tm/A at H0 = 100 A/m, Table 1) all show that strong volume pinning of DWs vanishes and the surface pinning becomes important. Since Mm/Ms ( 1, in the magnetization processes participates almost whole domain structure, and the participation of SDS shows up in the width of the maximum of dM/dt vs. H curve in Fig. 5b. The variation of logHc with log(Mm/Ms) for the annealed sample (Fig. 2a) is different from that for as prepared one and shows two distinctly different regimes depending on Mm/Ms >/< 0.9. For Mm/Ms ( 0.9 lower slope of logHc vs. log(Mm/Ms) indicates that weaker surface pinning centres affect the magnetizations processes in this region of Mm, whereas a rapid increase of Hc with Mm for Mm/Ms > 0.9 implies the stronger pinning of DWs. The variation of Mr with Mm/Ms is qualitatively the same as that of Hc and the absence of saturation of Mr at elevated Mm implies that irreversible motion of DWs is the main magnetization mechanism in both regimes (Mm/Ms > or < 0.9). Accordingly, we expect that SDS pinning may be relevant throughout the explored range of Mm (0.2 ( Mm/Ms ( 0.96). Fig. 6 shows the influence of static Hp on the parameters of the M-H loops of nanocrystalline FeCuNbSiB ribbon in the regime of stronger DW pinning centres (H0 = 100 A/m, Mm/Ms = 0.96). The coercive field Hc increases with Hp for both directions of JD, but its rate of increase is larger for Hp ( 5 A/m than that for Hp > 5 A/m. This is exactly the variation predicted by eqs. (5) and (7) for k ( tan(((. The continuous increase of Hc with Hp indicates that the enhanced surface pinning of DWs dominates the magnetization processes, whereas the appearance of two regimes ((A) and (B) in the model) with different variations of Hc with Hp, implies that the strength of pinning of DWs belonging to MDS is different at the opposite surfaces of the sample. The overall broadening of dM/dt vs. H curve at Hp = 24 A/m (Fig. 5b) seems to confirm the assumed influence of Hp on the surface domain structure, whereas the shift of sharp maxima towards higher magnetizing fields H reflects the enhanced pinning of DWs belonging to MDS, i.e. the increase of Hc (Fig. 5a). For Hp ( 5 A/m also the position of the center of the M-H loop C, varies linearly with Hp, which corresponds to regime A in the model (eqs. (5) and (6)), where Hc increases due to influence of Hp on the SDS only. Accordingly, (Hc/(Hp = k (eq. (5)) and from the data in Fig. 6 we estimate k ( 0.067. Slower increase of Hc with Hp for Hp > 5 A/m (regime B, eq. (7)) shows that the enhancement of SDS pinning of DWs overcomes the additional pressure on DWs due to projection P of Hp, i.e. kHp > Hptan <(> and (Hc/(Hp = k - tan <(> > 0 results. From the slopes of Hc vs. Hp variations for Hp < 5 A/m and Hp > 5 A/m in Fig. 6 we calculate the angle <(> ( 2.5(. The smallnes of angle <(> explains small direct influence of Hp on depinning of DWs of MDS, hence the increase of Hc with Hp (k > tan<(>). From the data in Fig. 6 by using eqs. (5) and (7) we also calculated the strengths of pinning of DWs (which sre responsible for Hc in the absence of Hp) at the opposite surfaces of the sample: Hsu0 = Hc0 = 1.3 A/m and Hsl0 = 1.6 A/m. By inserting the data for Hsu0 and Hsl0 in eq. (8) we find C = ( 0.15 A/m which agrees quite well with the experimental results for C around Hp = 5 A/m (Fig. 6). From the average slope (C/(Hp for Hp ( 5 A/m we obtained an independent estimate (eq. (6)) of angle <(> ( 1.5(. We note however that the experimental values of C are obtained by substracting two quantities (eq. (6)) with similar magnitudes which is subject to large errors. Because of this, we consider the agreement between two values of <(> quite good. However, for Hp > 5 A/m C does not seem quite constant (as predicted by eq. (8)) which may indicate that the enhancement of SDS pinning is not quite the same for two surfaces of the ribbon (ku ( kl). This would affect the variations of C and Hc for Hp > 5 A/m and may therefore contribute to the difference in the values of <(> determined from Hc(Hp) and C(Hp) respectively. Small decrease of Mm on increasing Hp ((Mm/Mm ( 0.02 for Hp = 24 A/m) is also consistent with the enhancement of SDS pinning on increasing Hp (Fig. 6). In particular, a fraction of the SDS domains with magnetizations locked in the direction of Hp contributes less to the magnetization of the sample along its axis. It is interesting to note that inspite of the continous increase of Hc with Hp the hysteresis loss E (the area of the M-H loop) for Hp ( 5 A/m continously decreases with Hp (inset to Fig. 5a). As illustrated in Fig. 5a for Hp = 24 A/m this occurs because the magnetization processes become almost reversible for (0M > 0.5 T ((H( ( 10 A/m) which reduces the overall area of the M-H loop in respect to that for Hp = 0. Therefore in nanocrystalline FeCuNbSiB ribbons the SDS pinning enhanced by Hp has detrimental influence on the magnetization processes at lower magnitudes of H (where the magnetization proceeds via irreversible motion of 180(-DWs separating MDS domains with magnetizations I forming small angles <(> with ribbon axis), whereas at higher H (hence M) Hp makes the magnetization processes almost reversible which results in lower overall hysteresis loss E. Accordingly, one expects particularly strong influence of Hp on the M-H loops and their parameters in the region of lower Mm magnitudes. The measurements performed in the region of weaker DW pinning (Mm/Ms = 0.66 and Hc0 = 0.74 A/m for H0 = 10 A/m) confirm these expectations (Fig. 7). As seen from Fig. 7, the variations of Hc, Mm and C with static Hp are qualitatively the same as those for H0 = 100 A/m (Mm/Ms = 0.96) in Fig. 6, which means that also here SDS pinning dominates the magnetization processes. In particular, the coercive field increases with Hp and this increase is faster for Hp ( 5 A/m than that for Hp > 5 A/m. From the experimental Hc vs. Hp variations (Fig. 6) we extract (by the use of eqs. (5) (8)) k = 0.07 and <(> = 2.4( which agree well with the corresponding results obtained for Mm/Ms = 0.96. Simultaneously, Mm considerably decreases with Hp and, inspite of a scatter of the data, the variation of C with Hp is similar to that shown in Fig. 6. We note however that the total change of Hc ((Hc/Hc0 ( 1.1) and Mm ((Mm/Mm ( 0.42) is much larger than that observed for Mm/Ms = 0.96 over the same range of Hp = 24 A/m (Fig. 6). This confirms particularly strong influence of the SDS pinning on the magnetization processes in the region of lower magnetizing fields. Next we briefly examine the influence of dynamic surface field on the coercive field and the position of the center of the M-H loop for the same sample and H0 = 100 A/m. Fig. 7 shows that both for suitable phase of JA (Fig. 1) and unsuitable one Hc increases with Hp0 which lends further support to the assumption of enhanced SDS pinning of DWs in the presence of Hp. In particular, the increase of Hc with Hp0 for the suitable phase of JA is approximately linear in accord with eq. (13) and the data yield (Hc/(Hp0 = k - tan <(> = 0.026. For the unsuitable phase of JA the variation of Hc with Hp0 shows two different regimes (due to Hsl0 ( Hsu0) depending on the magnitude of Hp0: for Hp0 ( 5 A/m Hc increases rapidly with Hp0 and applying eq. (14) to the data in Fig. 8 we find (Hc/(Hp0 = k + tan <(> = 0.11; for Hp0 > 5 A/m the increase of Hc with Hp0 is slower and the interpretation of the experimental data in terms of eq. (15) yields (Hc/(Hp0 = k - tan <(> = 0.034. From the results for unsuitable phase of JA we obtain k = 0.072 and <(> = 2.2( whereas from the combination of the results for suitable and unsuitable phase of JA for Hp0 ( 5 A/m k = 0.068 and <(> = 2.4( is found. Therefore, the influence of dynamic Hp (for both phases of JA) on Hc is also consistent with the model (eqs. (13) (15)) and yields the same parameters k and <(> as those calculated from the effects of static Hp on Hc and C of the same sample. The center of the M H loop is not influenced with Hp0 (C ( 0, Fig. 8) which is also consistent with the model. Conclusions The influence of static and dynamic surface fields Hp (generated by the core currents) on the parameters (Hc, Mm) of the M H loops of optimally annealed FeCuNbSiB ribbons is distinctly different from that which is commonly observed for amorphous soft ferromagnetic ribbons (including the FeCuNbSiB ribbon in the amorphous state). In particular, for nanocrystalline FeCuNbSiB ribbons Hc continously increases with Hp whereas for other soft magnetic ribbons it decreases with Hp [3]. We propose that this phenomenon occurs due to strong interplay of the main (inner) domain structure (MDS) and surface domain structure (SDS). More preciselly, the pinning of DWs belonging to MDS due to surface domains (SDS pinning [15]) is enhanced in the presence of Hp (which tends to fix and/or rotate the magnetization of SDS domains forming large angles with ribbon axis). This enhanced SDS pinning becomes the dominant mechanism for pinning of DWs in the soft ferromagnetic ribbons exhibiting very low intrinsic pinning. Accordingly, we developed simple model which includes the influence of SDS pinning on the magnetization of the ribbon under simultaneous influence of the magnetizing field H and Hp. Detailed analysis of the influence of static and dynamic Hp on Hc, Mm and C of nanocrystalline FeCuNbSiB ribbon for two different amplitudes of H (H0 = 10 A/m and 100 A/m respectively) hence in different regions of Mm, agrees very well with the model predictions. In particular, the analysis shows that the enhancement of SDS pinning of DWs due to Hp overcomes the direct influence of Hp (i.e. of its projection P = Hpsin<(>) on the DWs belonging to MDS, hence the increase of Hc with Hp. Although the enhancement of the SDS pinning by Hp should be quite general phenomenon for ferromagnetic ribbons, its effects become apparent only when the intrinsic pinning of DWs is very weak and the magnetizations of the MDS domains form very small angles ((( with the ribbon axis. Indeed, the preliminary measurements [7] of the influence of Hp on the magnetization processes in amorphous VITROVC 6026Z ribbon (which has similar domain structure and intrinsic pinning as nanocrystalline FeCuNbSiB ribbons) show that the effects of Hp on the parameters of the M-H loop are similar to those described in this paper. The above findings are important for the correct evaluation of the performance of such materials in the situations in which they are exposed to external fields with complex configurations. In particular, the unfavourable field configuration (similar to that in this work) can seriously deteriorate their soft magnetic properties even at low amplitudes of the external field. We wish to emphasize that the proposed model in addition to providing an insight into the nature and mechanism of DW pinning in soft ferromagnetic ribbons also enables a quantitative determination of the important characteristic of these materials such as the strength of intrinsic DW pinning (Hsu0, Hsl0), the pinning inhomogeneity (Hsu0 > or < Hsl0) and the magnetization anisotropy (<(>). The knowledge of these data is necessary in order to select the best methods for the improvement of their magnetic properties. In particular, for the investigated FeCuNbSiB ribbon the introduction of an uniaxial anisotropy which would increase somewhat the angle <(> (for instance by field annealing, or surface treatment [20]) would simultaneously decrease the influence of Hp on SDS pinning and increase the influence of Hp on DWs of MDS. More precisely, since k ( 0.07 was found for the studied sample, already for the angles <(> > 4(, k < tan <(> results and both static and dynamic Hp ( 5 A/m should decrease Hc (eqs. (7), (13) and (15)). Acknowledgement We wish to thank to Dr. G. Herzer for giving us FeCuNbSiB samples. References [1] C. Aroca, E. Lopez, P.S. Sanchez, J. Magn. Magn. Mater. 23 (1981) 193. [2] R.N.G. Dalpadado, IEEE Trans. Magn. 17 (1981) 3163. [3] S. Sabolek, E. Babi and K. Zadro, Fizika A 1 (1992) 167. [4] S. Sabolek, J. Horvat, E. Babi, K. Zadro, J. Magn. Magn. Mater. 110 (1992) L25. [5] S. Sabolek, E. Babi, }. Marohni, Phys. Rev. B 48 (1993) 6206. [6] S. Sabolek, IEEE Trans. Mgn. Mag 30 (1994) 925. [7] S. Sabolek, E. Babi, D. Posedel, M. `uaak, Sensors and Actuators A 106 (2003) 65. [8] J. Horvat, }. Marohni, E. Babi, J. Magn. Magn. Mater. 82 (1989) 5. (9( Y. Obi, H. Fujimori, E. Lopez, IEEE Trans. Magn. 17 (1981) 1462. (10( G. Schroeder, R. Schfer, H. Kronmller, J. Magn. Magn. Mater. 60 (1986) 182. (11( H. J. de Wit, M. Brouha, J. Appl. Phys. 57 (1985) 3560. (12( P. Schnhuber, H. Pftzner, G. Harasko, T. Klinger, K. Futschik, J. Magn. Magn. Mater. 112 (1992) 349. [13] A. Zelenakova, P. Kollar, M. Kuzminski, M. Kollarova, Z. Vertesy, W. Riehemann, J. Magn. Magn. Mater. 254 255 (2003) 152. (14( J. J. Becker, J. Appl. Phys. 52 (1981) 1905. (15( K. H. Stewart, Ferromagnetic Domains (Cambridge University Press, Cambridge, 1954) p. 165. [16] H. Kronmller, J. Magn. Magn. Mater. 24 (1981) 159. [17] J. Horvat, E. Babi, }. Marohni, H.H. Liebermann, J. Magn. Magn. Mater. 87 (1990) 339. [18] B. Hofman, T. Reininger, H. Kronmller, phys. Stat. sol. (a) 134 (1992) 247. [19] G. Herzer, Physica Scripta T 49 (1993) 307. [20] S. Sabolek, E. Babi, S. Popovi, }. Marohni, J. Magn. Magn. Mater. 291 (2003) 269.  Fig.  SEQ Figure \* ARABIC 1. Schematic drawing of the domain wall DW, domain magnetizations I, applied field H and surface fields Hp generated by the core current JD. The inset: drive field (dotted) alternating core current relationship.  Fig.  SEQ Figure \* ARABIC 2. Variation of the coercive field Hc (a) and remanent magnetization Mr (b) with the normalized magnetization Mm/Ms before annealing (open symbols) and after annealing at temperature Ta = 540(C (solid symbols) for the Fe73.5Cu1Nb3Si15.5B7 ribbon. A triangular drive field H with the frequency f = 5.5 Hz and different amplitudes H0 ( 350 A/m was used.  Fig.  SEQ Figure \* ARABIC 3. Variation of the coercive field Hc (%), maximum magnetization (0Mm (() and the position of the center of the M - H loop C (() with the magnitude of static surface field Hp for the Fe73.5Cu1Nb3Si15.5B7 ribbon in the amorphous state. A triangular drive field H with the frequency f = 5.5 Hz and the amplitude H0 = 100 A/m was used.  Fig. 4. Variation of the coercive field Hc (%), maximum magnetization (0Mm (() and the position of the center of the M - H loop C (() with the magnitude of static surface field Hp for the Fe73.5Cu1Nb3Si15.5B7 ribbon in the amorphous state. A triangular drive field H with the frequency f = 5.5 Hz and the amplitude H0 = 25 A/m was used.  Fig. 5. 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$dha$gdI$7dh`7a$gdtΉ !"#$9fgijˊ.b̋*,.02<Z\̍ĽĽĽĽĹĵĵĵĪhH h^`h#ah#amHsHh#a h^`hp-hp-h^` h^`hx.hx.hDZ j]hIhI j[hIh}h}mHsH h^`h}h}mHsHh} h\\ h6\h}h}\4\Џҏԏ֏؏ڏ܏ޏgdfzdhgdZLΏЏҏԏ %&',-CDEFGHIRmp˽xxix^RFh1h]T5CJaJh1hkQ5CJaJh1hCJaJho5CJaJmHnHu jh1h5CJUaJh1h5CJaJhjRhUjhUmHnHujhkQUmHnHujh.UmHnHuhW hfzhfzhfzh (()(max (Tm/A) Fe73.5Cu1Nb3Si15.5B7Prean.13.50.402.49.7(10 4After an.1.30.962.59.8(10 4Table  SEQ Table \* ARABIC 1 Data relevant to Fe73.5Cu1Nb3Si15.5B7 sample before annealing and after annealing at Ta = 540(C: Hc0, Mm/Ms and (max are the coercive field, normalized maximum magnetization and maximum permeability, respectively, in the absence of surface fields. <(> is the average angle between the magnetization of the domains and the ribbon axis deduced from the variations of the Hc and C with the static surface field Hp. A triangular drive field H with the amplitude H0 = 100 A/m and frequency f = 5.5 Hz was used. 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