Research Article | Open Access

Dawei Xing, Dongming Chen, Fang Liu, Jingshun Liu, Hongxian Shen, Zhiliang Ning, Fuyang Cao, Jianfei Sun, "Torsion Dependence of Domain Transition and MI Effect of Melt-Extracted Co_{68.15}Fe_{4.35}Si_{12.25}B_{13.25}Nb_{1}Cu_{1} Microwires", *Advances in Materials Science and Engineering*, vol. 2015, Article ID 958341, 6 pages, 2015. https://doi.org/10.1155/2015/958341

# Torsion Dependence of Domain Transition and MI Effect of Melt-Extracted Co_{68.15}Fe_{4.35}Si_{12.25}B_{13.25}Nb_{1}Cu_{1} Microwires

**Academic Editor:**You Song

#### Abstract

We present the torsional stress induced magnetoimpedance (MI) effect and surface domain structure evolution of magnetostrictive melt-extracted Co_{68.15}Fe_{4.35}Si_{12.25}B_{13.25}Nb_{1}Cu_{1} microwires. Experimental results indicate that the surface domain structures observed by magnetic force microscope (MFM) transform from the weak circumferential domain of as-cast state to the helical domain under large torsional strain of 81.6 (2*π* rad/m). Domain wall movement distorts at torsional strain (2*π* rad/m) and forms a helical anisotropy with an angle of around 30° versus axial direction of wire. At 15 MHz, the maximum of GMI ratio (%) increases to 194.4% at (2*π* rad/m) from 116.3% of the as-cast state and then decreases to 134.9% at (2*π* rad/m). The torsion magnetoimpedance (TMI) ratio (%) is up to 290%. Based on this large torsional strain and high MI ratio, the microwire can be as an referred candidate for high-performance TMI sensor application.

#### 1. Introduction

The ferromagnetic microwires have been recognized as possessing much more promising magnetic sensing materials, especially for giant magnetoimpedance (GMI) effect, which has attracted considerable interest not only from the basically theoretical viewpoint but also from its wide technical applicability [1–4]. As well known, the near-zero magnetostrictive wires with soft magnetic properties have high MI ratios [1, 5]. As one method of the amorphous microwire fabrication technologies, different from glass-coated spinning and in-rotating water quenching techniques, the melt-extraction technique consists of the following: (i) it has the largest solidification or cooling rate, which enables the wires to possess an excellent soft magnetic property; (ii) the melt-extracted wires without glass covering are more suitable for electronic package and GMI sensor applications; (iii) the parameters (i.e., linear velocity of wheel, feed rate of the molten, etc.) of melt-extraction can be conveniently controlled to produce wires with uniform diameter and roundness [6, 7]. In another perspective, near-zero magnetostrictive amorphous wires, with low resistivity , high magnetic permeability , high saturation magnetization , and small ferromagnetic resonance (FR) in the high-frequency range, possess outstanding GMI performance. Based on this principle, the element B in CoFeSiB alloy is substituted for Nb and Cu with low resistivity materials and a small amount of atomic percentage 1% and 1%, respectively.

In the meantime, in the intermediate frequency range (100 kHz~20 MHz), GMI originates mainly from the variation of the skin depth owing to the strong changes of the effective magnetic permeability resulting in both domain wall motion and magnetization rotation; namely, it can be denoted by [1, 8]. The role of gives rise to the helical anisotropy change. In order to understand deeply the role of the helical anisotropy to the surface domain and GMI performance of the near-zero magnetostrictive melt-extracted Co-based amorphous microwires, the imposed torsional strain on the microwires is necessary to observe the domain structure by magnetic force microscope (MFM) and modify the domain transition for MI and torsion magnetoimpedance (TMI) sensor application.

Up to now, much works have previously reported the influence of torsion on MI effect for Co-based and Fe-based glass-coated or in-rotating water amorphous wires [9–13]. Betancourt and Valenzuel found the an asymmetric behavior dependent on the direction of the applied torsion strain of in-rotating water (Co_{94}Fe_{6})_{72.5}B_{15}Si_{12.5} wires [9]. Garcia et al. studied the magnetoimpedance response under tensile and torsional stress of Fe_{76}B_{13}Si_{11} glass-coated amorphous microwires and induced a helical magnetic anisotropy that modifies the magnetic domain structure and the magnetic response of the sample applied torsion stresses [10]. Popov et al. proposed the “enhanced core-shell” model of vanishing-magnetostrictive glass-coated Co-rich microwires to resolve the physical origin of the low-field hysteresis and the dependence of induced anisotropy field on the applied tensile and/or torsional stress [11]. However, only a few researchers resorted to the surface domain structure (SDM) of twisted microwire to explore the detailed information of the modified domain and the helical anisotropy.

As well known, the core-shell magnetic structures of nearly zero magnetostrictive melt-extracted Co-based amorphous wires consist of a cylindrical inner core domain oriented axially and the outer shell domain for circumferential magnetization, while the exchange energy tilts it towards a helical orientation [14]. Generally, GMI effect is very sensitive to the magnetic structure and the local anisotropies of soft magnetic materials. It It can be additionally served as a powerful tool to explore the important information of the magnetic structure and local anisotropies. Moreover, the domain structure and anisotropy field of the magnetic materials can be derived from analyzing the corresponding changes of GMI property of samples subjected to stress applied. The modification of GMI response is the consequence of the competition between the helical anisotropy introduced by the applied torsional stress and the internal anisotropies. Therefore, torsional stresses were found to modify the magnetization cycle of the wire [15], Young’s modulus [16] and MI response [11], and so forth.

The aim of this work is conducted to study the static surface magnetic domain structure, MI effect of a nearly zero magnetostrictive melt-extracted Co-rich amorphous microwire dependence on applied extremely huge torsional strain and to obtain large MI value by modulating the magnetic structure and local anisotropies of soft magnetic microwires for potentially exploring the torsion MI sensors.

#### 2. Experimental

We have prepared softly magnetic amorphous microwires of Co_{68.15}Fe_{4.35}Si_{12.25}B_{13.25}Nb_{1}Cu_{1} with diameter of 35 *μ*m by a modified melt-extraction technique [6]. Impedance measurement is carried out at the intermediate frequency range of 100 kHz~15 MHz by using Agilent 4294A precision impedance analyzer. The MR, MX, and MI ratios are defined as follows, respectively:

The total length of each microwire is 58 mm under the application of a torsional strain ranging from 0 to 102.0 (2*π* rad/m) with the one end fixed and the other end rotating in clockwise direction. Then, we selected the central part of 18 mm long microwire to connect to the circuit and to measure the MI effect by the driving amplitude of 20 mA with DC axial field applied by using a pair of Helmholtz coils. The external field is up to the maximum of 80 Oe. The Helmholtz coil was kept perpendicular to the earth’s magnetic field direction.

The torsion magnetoimpedance (TMI) ratio, , or the relative change of the maximum magnetoimpedance with the torsion is expressed as follows:
where (2*π* rad/m) and the external field is 0 Oe.

Domain observation of microwire is conducted by a Nanoscope III multimode atomic force microscope from Digital Instruments. The micro-etched silicon probe tip is to collect related information by using a combination of tapping and lift mode. During lift mode, the magnetic data were collected and displayed.

#### 3. Results and Discussion

It has been known that the changes of both resistance and reactance depending on and external field will alter the impedance and therefore are contributed to GMI behavior [1]. Based on the expression of the impedance of cylindrical magnetic conductor, with is expressed in terms of first order Bessel functions , and the material parameters: the skin depth , the radius , and the dc resistance of the conductor. The skin depth , , where is the resistivity of the conductor and is the current frequency, and the is circumferential permeability. The resistance and reactance can be depicted as: ; , where and are the vacuum permeability and the average relative circumferential permeability, respectively [1].

Figure 1 shows the zero-field frequency dependence of resistance (a), reactance (b), and impedance (c) of microwires with torsion strain from as-cast to 102.0 (2*π* rad/m). An obvious monotonic increase in the resistance (as shown in Figure 1(a)), inductive reactance (Figure 1(b)), and impedance (Figure 1(c)) is observed with the frequency range of 100 kHz~15 MHz for the skin effect. And the maximum of each of , , and values is 477.7 Ω, 297.1 Ω, and 562.5 Ω, respectively, as the torsional strain increased to 20.4 (2*π* rad/m). Continued to increase the torsion strain up to 40.8~102.0 (2*π* rad/m), all the values of , , and curves decrease. Additionally, the curves of (, , and ) at torsional strain of 20.4 (2*π* rad/m) have a very small difference with curves of 40.8 (2*π* rad/m). Also a similar behavior displays between curves of 81.2 (2*π* rad/m) torsional strain with 102.0 (2*π* rad/m) torsional strain. At the intermediate frequency regime, skin effect is dominant and the impedance is proportional to the square root of frequency and circumferential permeability; namely, . The influence of torsion stress on the microwire will improve the circular permeability at a certain extent. Therefore, the corresponding values of , , and for the torsional microwires all increase with the frequency.

**(a)**

**(b)**

**(c)**

Figure 2 reveals the magnetic field dependence of the magnetoresistance (Figure 2(a)), magnetoinductive reactance (Figure 2(b)), and magnetoimpedance (Figure 2(c)) ratios at = 15 MHz for applied torsion from 0 to 102.0 (2*π* rad/m). In comparison with the behavior of and , the curves of (Figure 2(b)) appear to the peaks with positions from 0.4 Oe to 0.7 Oe for torsion strain from 20.4 (2*π* rad/m) to 102.0 (2*π* rad/m). This torsion stress can be considered to change greatly the permeability. In addition, this response of the microwire is attributed to two magnetization processes: spin rotation and bulging of pinned domain walls. As shown in Figure 2(c), the curves of also exhibit the increasing trend at (2*π* rad/m) and then decrease with the to 102.0 (2*π* rad/m). The magnified plot of the peak value of inserted in the Figure 2(c) displays the ratio of from 116.2% at as-cast to 194.4% at (2*π* rad/m) for = 15 MHz. This enhanced improvement can be attributed to the releasing residual stress and the modified surface domain structure, as shown in Figure 3(b).

**(a)**

**(b)**

**(c)**

**(a)**

**(b)**

**(c)**

**(d)**

The behavior of GMI profiles is well resolved by considering the domain model with periodically circular domains [17]. Large is contributed to the high GMI ratio and well-defined circumferential domain structure [18]. Therefore, we can improve the circumferential permeability and impedance by modulating the surface domain structure.

Accordingly, the surface morphology, domain structure obtained by MFM, and the schematic plot of microwire are presented for untwisted and under torsional strain state in Figure 3. The surface domain structure of the microwire of as-cast state is showed in Figure 3(a). The ill-defined circumferential domain configuration is exhibited with the average domain width of about 1.0 *μ*m. The weak and uneven circumferential domain on the whole surface result from the microwire preparation process and the weak circular magnetic anisotropy. The residual stress and even heterogeneous microstructure of microwire all are not conducive to the formation of circumferential domain. So the corresponding the ratio of is only 116.2%. In order to induce helical anisotropy and further to influence the magneto-impedance response, each microwire was submitted to a homogenous torsional stress to form even domain structure. The modification of domain structure with increasingly applied torsion is obtained in Figures 3(b), 3(c), and 3(d). For (2*π* rad/m), the surface morphology of the microwire appears distortion for the surface roughness of dozens of nanometers. Moreover, the domain structure was observed clearly with torsion stress applied to the wire in middle part of Figure 3(b). Different from the weak circumferential domain of as-cast state, the surface domain with the torsional state (2*π* rad/m) turns to form the zigzag domain, which is derived from the helical anisotropy. The relatively large GMI ratio on this stage is contributed from the enhanced circumferential anisotropy generated by circular component of torsion stress. Additionally, the circumferential component of helical anisotropy induced by applied the torsional stress improves the circular anisotropy, which is benefit for circumferential permeability , further for GMI ratios improvement. Consequently, the average domain width increases to 1.1 *μ*m at (2*π* rad/m). For this circumstance, the circumferential domain turns to zigzag domain under the torsional strain, at which behavior is different from the consistency deflection for positive magnetostrictive Fe-based wires [19]. As the applied torsion increases to 61.2 (2*π* rad/m) in Figure 3(c), the uneven domain is changed into more clear domain and smooth domain wall with average width about 0.9 *μ*m and tilt angle up to about 67°. Further to apply the torsional strain to 81.6 (2*π* rad/m), the uniform helical domain is obtained with domain wall angle . Based on the extreme torsion applied, GMI profile exhibits the maximum of 139.4% at (2*π* rad/m). The slight difference between GMI ratios of (2*π* rad/m) and (2*π* rad/m) indicates the surface domain in each case is very similar. Momently, a uniform helical domain is therefore formed with smaller domain wall angle of , at which performance manifests the homogeneous and larger helical anisotropy. Additionally, an interesting result of Co-based melt-extracted microwires with large torsion strain performance of (2*π* rad/m) will be as the ideal candidate potential materials for high-performance torsion TMI sensor [20].

To sum up, the torsional strain dependence of torsional impedance profile and domain wall angle is illustrated in Figure 4. As observed, the ratios decrease with the increasing torsional strain . The maximum ratio is up to 290%. Combining with the domain transformation applied different torsional strain (Figure 3), the domain wall movement is neither ideally towards longitudinal nor uniformly with a helical component along the axial direction. The domain wall distortion firstly is perpendicular to the axial direction (Figure 3(b)) and then tilts to transverse direction with a small angle (Figure 3(c)) and forms a helical magnetic anisotropy making an angle about 30° with the longitudinal direction (Figure 3(d)). So the large torsional strain is up to 102.0 (2*π* rad/m) as the candidate for torsion magnetoimpedance (TSI) application.

#### 4. Summary

In conclusion, we have systematically investigated the surface domain transition and MI effect of Co-based melt-extracted microwires at different torsional strain. Firstly, the Co-based microwire is revealed to achieve the huge torsion strain behavior of (2*π* rad/m). We also observed an increased MI ratio as a result of modification of the helical magnetic anisotropy. Accordingly, the domain transformation under torsion stress corresponding to the GMI profile exhibits the heterogeneous transition. And the obtained results on large torsion magnetoimpedance ratio to 290% can be suitable for further development of the high-performance torque TSI sensors.

#### Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

#### Acknowledgments

Dawei Xing acknowledges the financial support provided by the Natural Science Foundation of China (NSFC) under Grant no. 51371067. Jingshun Liu acknowledges the supports from NSFC with Grant no. 51401111, Natural Science Foundation of Inner Mongolia Autonomous Region of China under Grant no. 2014BS0503, and Scientific Research Foundation of the Higher Education Institutions (SRFHEI) of Inner Mongolia Autonomous Region of China under Grant no. NJZY14062.

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#### Copyright

Copyright © 2015 Dawei Xing et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.