**The Coupled Magnetic Field Effects on the Microstructure Evolution and Magnetic Properties of As-Deposited and Post-Annealed Nano-Scaled Co-Based Films — Part I**

Donggang Li, Qiang Wang, Agnieszka Franczak, Alexandra Levesque and Jean-Paul Chopart

Additional information is available at the end of the chapter

http://dx.doi.org/10.5772/61270

#### **Abstract**

Superimposed external magnetic fields during electrodeposition process offers the possibility to tailor microstructure and properties of the obtained films in a very effi‐ cient, contactless, and easily controllable way, what is caused by so-called magnetohy‐ drodynamic (MHD) effect. On the other hand, the nonequilibrium state of aselectrodeposited nanocrystalline films provides a strong thermodynamic potential for microstructural transformation. This means that the benefit effect of magneto-electro‐ deposition on a nanocrystalline film can be completely consumed by a thermal expo‐ sure at relatively low temperature. Magnetic field annealing has been confirmed to be useful for tailoring the microstructure of as-deposited nanocrystalline films for their widespread uses.

The particular interest of this book Chapter "Growth of Co-based magnetic thin films by magnetic fields (MF) assisted electrodeposition and heat treatment" is the finding that the microstructure and magnetic properties of nanocrystalline Co-based alloys and oxides like CoX (X= Cu, Ni, NiP, FeO) are improved by imposition of MF during elaboration process or post-annealing process. According to the previous study, the targeted scientific activities pay more attention to develop alloys and oxides in nanoscale using pulsed electrodeposition assisted by high magnetic field (HMF). (Note: Since the instantaneous current density during pulse electrodeposition is higher than that during direct current plating, the microstructure of the nano-scale electrodeposits can be more easily controlled by perturbing the desorption/adsorption processes oc‐ curring in the pulse electrodeposition process).

During the experiment, high magnetic field is an in-situ method for the control of electrodeposition process. The obtained material is then annealed or oxidized after

© 2015 The Author(s). Licensee InTech. This chapter is distributed under the terms of the Creative Commons Attribution License (http://creativecommons.org/licenses/by/3.0), which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

elaboration under HMF. Comparative studies are performed concerning the electro‐ deposition process in a high magnetic field, by changing the magnetic field parame‐ ters such as magnetic flux density, direction, gradient. Then, we will investigate the evolution of the microstructure induced by magnetic field, and the control of crystal orientation, crystal size, and its distribution by a HMF. By comparing the microstruc‐ ture and magnetic properties of the film with and without a HMF, we can find opti‐ mum magnetic field parameters for the control of the growth of nanocrystalline Cobased magnetic film. The functionality of materials could then be improved by both processes under HMF: electrodeposition and annealing.

**Keywords:** coupled magnetic field effects, microstructure evolution, nano-scaled Cobased films

## **1. High magnetic field annealing dependent on the morphology and microstructure of electrodeposited Co/Ni bilayered films**

#### **1.1. Introduction**

Electrodeposited nanocrystalline magnetic films have received considerable interest in the fields of data storage devices and microelectromechanical systems (MEMS) [1], since the microstructure of the film can be easily controlled on a large scale during the electrochemical processing in comparison with a physical vapor deposition. It is well known that the physical properties of the electrodeposits strongly depend on morphology and microstructure, as reported in recent papers [2-3]. Numerous studies have been devoted to improve surface morphology and microstructure, i.e., reducing the grain size and the roughness, by magneto‐ hydrodynamic effect (MHD), which is induced by superimposing an external magnetic field [4-6] during the electrodeposition process. However, the nonequilibrium state of as-electro‐ deposited nanocrystalline layers provides a strong thermodynamic potential for microstruc‐ tural transformation. This means that the benefit effect of magneto-electrodeposition on a nanocrystalline film can be completely consumed by a thermal exposure at relatively low temperature [7]. Magnetic field annealing has been confirmed to be useful for tailoring the microstructure of as-deposited nanocrystalline films for their widespread uses [8]. Markou et al. [9] obtained a high-degree (001) texture in L10 CoPt films by annealing Co/Pt bilayers in a perpendicular magnetic field of 1 kOe. The advancement of superconducting technology has opened unique aspects for heat treatment in a high magnetic field. Up to date, few applications of high magnetic field (over 10 T) during annealing process [10] proved it to be a promising method to control the preferential crystallographic orientation of the deposited magnetic film. Though there is no doubt that high magnetic field annealing plays an important role on grain growth, inter-diffusion [11-13], and recrystallization processes, which in turn will influence the microstructural variation of nanocrystalline film, the dependences of grain shape, grain size, roughness, and texture of electrodeposited films on the magnetic field parameters during post-annealing are still unclear. In this study, we investigate the effect of post-high magnetic field annealing up to 12 T on Co/Ni bilayered film obtained by electrodeposition assisted with or without a 0.5 T magnetic field.

## **1.2. Experimental**

elaboration under HMF. Comparative studies are performed concerning the electro‐ deposition process in a high magnetic field, by changing the magnetic field parame‐ ters such as magnetic flux density, direction, gradient. Then, we will investigate the evolution of the microstructure induced by magnetic field, and the control of crystal orientation, crystal size, and its distribution by a HMF. By comparing the microstruc‐ ture and magnetic properties of the film with and without a HMF, we can find opti‐ mum magnetic field parameters for the control of the growth of nanocrystalline Cobased magnetic film. The functionality of materials could then be improved by both

**Keywords:** coupled magnetic field effects, microstructure evolution, nano-scaled Co-

**1. High magnetic field annealing dependent on the morphology and**

Electrodeposited nanocrystalline magnetic films have received considerable interest in the fields of data storage devices and microelectromechanical systems (MEMS) [1], since the microstructure of the film can be easily controlled on a large scale during the electrochemical processing in comparison with a physical vapor deposition. It is well known that the physical properties of the electrodeposits strongly depend on morphology and microstructure, as reported in recent papers [2-3]. Numerous studies have been devoted to improve surface morphology and microstructure, i.e., reducing the grain size and the roughness, by magneto‐ hydrodynamic effect (MHD), which is induced by superimposing an external magnetic field [4-6] during the electrodeposition process. However, the nonequilibrium state of as-electro‐ deposited nanocrystalline layers provides a strong thermodynamic potential for microstruc‐ tural transformation. This means that the benefit effect of magneto-electrodeposition on a nanocrystalline film can be completely consumed by a thermal exposure at relatively low temperature [7]. Magnetic field annealing has been confirmed to be useful for tailoring the microstructure of as-deposited nanocrystalline films for their widespread uses [8]. Markou et al. [9] obtained a high-degree (001) texture in L10 CoPt films by annealing Co/Pt bilayers in a perpendicular magnetic field of 1 kOe. The advancement of superconducting technology has opened unique aspects for heat treatment in a high magnetic field. Up to date, few applications of high magnetic field (over 10 T) during annealing process [10] proved it to be a promising method to control the preferential crystallographic orientation of the deposited magnetic film. Though there is no doubt that high magnetic field annealing plays an important role on grain growth, inter-diffusion [11-13], and recrystallization processes, which in turn will influence the microstructural variation of nanocrystalline film, the dependences of grain shape, grain size, roughness, and texture of electrodeposited films on the magnetic field parameters during post-annealing are still unclear. In this study, we investigate the effect of post-high magnetic

**microstructure of electrodeposited Co/Ni bilayered films**

processes under HMF: electrodeposition and annealing.

based films

260 Electroplating of Nanostructures

**1.1. Introduction**

Nanocrystalline bilayered films were electrodeposited on ITO (1000 nm thickness)/ glass (1 cm2 ) with the structure of ITO glass/Ni/Co from two cells step by step. One cell contained the electrolyte of nickel sulfate 0.6 M, boric acid 0.4 M, and pH was adjusted to 2.7 at 30℃. The electrolyte in the other cell consisted of cobalt sulfate 0.6 M, boric acid 0.4 M, at 50℃, pH = 4.7. The counter electrode was a rectangular Pt plate of 1×2*cm*, placed parallel to the working electrode. Chronopotentiometry method with a current density of 10 mA /cm2 was performed for 6 min in Ni2+ cell, and 4 min in Co2+ cell, respectively. A water-cooled electromagnet was used to produce a magnetic field of 0.5 T. The magnetic field was superimposed parallel to the working electrode during the electrodeposition processing of Co film. Two series of electro‐ deposits were denoted, 0 T-Bed and 0.5 T-Bed.

The two series of as-deposited films were heat-treated at 673 K for 4 h under a protective atmosphere of high-purity argon in a vertical furnace, which was placed inside a supercon‐ ducting magnet of up to 12 T, and then cooled down to room temperature. The direction of the high magnetic fields was vertically upward, in perpendicular to the horizontally placed films, while the strengths of the magnetic fields were 0, 6, and 12T, respectively.

The surfacial morphology of the Co/Ni films was observed by using a field emission scanning electronic microscopy (FE-SEM, SUPRA 35) made in Japan with high magnification times. The topography and the roughness were investigated by the AFM (NTEGRA AURA, NT-MDT, Russia). Each sample was measured in areas of 10*μm*×10*μm* for three times at different positions of the film to obtain the average grain size and roughness of the surface. For the characterization of the films microstructure, Grazing Incidence X-Ray Diffraction (GI-XRD, Ultima IV, Japan) measurements were performed using the Cu *Kα* radiation (40 kV, 40 mA,

*λ* =1.54*A*). X-ray photoelectron spectroscopy (XPS) measurement (ESCALAB250, Thermo VG Company, USA) was done to analyze the distribution of Co and Ni along the cross-section of the samples, by which the thickness of Co layer can also be estimated as about 1200 nm.

#### **1.3. Results and discussion**

The FE-SEM images in Figure 1 show the surface morphology of annealed Co/Ni films under high magnetic fields of 0, 6, 12 T. By comparing the Figure 1(a1-a3) and Figure 1 (b2-b3), it can be seen that the application of high magnetic field annealing played a similar role on the morphological evolution in both series: 0 T-Bed and 0.5 T-Bed, although there is a obvious difference between the two series, which were annealed at the same 6 T magnetic field condition. It is generally considered that the effects of a weak magnetic field (Bed) on the morphology of electrodeposits were almost fully consumed by an annealing process for a long time. The films after post-annealed under 0 T magnetic field present a blurred irregular grain shape with a mass of velour-like deposits on the grain boundary. With the increase of the applied magnetic field, not only the grain shape and grain boundary become clear to form

mechanism needs further investigation.

bilayered film, AFM top view ( <sup>2</sup> 1010

seemed smaller than that of the annealed film under a no-field condition.

polyhedral grains but also the grain size decreases with the disappearance of the velour-like deposits.

**Figure 1.** FE-SEM images of 0 T-Bed series Co/Ni film annealed under different magnetic fields (a1) 0 T, (a2) 6 T, (a3) 12 T; and 0.5 T-Bed series annealed under (b1) 0 T, (b2) 6 T, (b3) 12 T. [48] **Figure 1.** FE-SEM images of 0 T-Bed series Co/Ni film annealed under different magnetic fields (a1) 0 T, (a2) 6 T, (a3) 12 T; and 0.5 T-Bed series annealed under (b1) 0 T, (b2) 6 T, (b3) 12 T. [48]

As it is well known, for magnetic and paramagnetic materials, magnetic field will induce a pulling force due to the magnetization [14–15], which force is favored for the separation of grains. In the meantime, an introduction of the magnetization energy during the magnetic field annealing results in the decrease of diffusion activation energy, which will improve the diffusion of the congregated deposits on the grain boundary. This is a possible reason for the grain boundary becoming clear after post-magnetic field annealing. Another most likely reason for the disappearance of velour-like product, which is estimated to be Co-oxides formed at the grain boundaries, is that the application of high magnetic fields during annealing process is favorable for the reduction of oxides, but the As it is well known, for magnetic and paramagnetic materials, magnetic field will induce a pulling force due to the magnetization [14-15], which force is favored for the separation of grains. In the meantime, an introduction of the magnetization energy during the magnetic field annealing results in the decrease of diffusion activation energy, which will improve the diffusion of the congregated deposits on the grain boundary. This is a possible reason for the grain boundary becoming clear after post-magnetic field annealing. Another most likely reason for the disappearance of velour-like product, which is estimated to be Co-oxides formed at the grain boundaries, is that the application of high magnetic fields during annealing process is favorable for the reduction of oxides, but the mechanism needs further investigation.

On the other hand, we should also take into account the effect of the magnetic field annealing on recrystallization process and grain boundary migration (GBM) in the films. If magnetic field annealing plays a retarded effect on the recrystallization process as reported by Refs. [16–17] or beneficial effects on GBM due to magnetic ordering as reported by Molodov et al [18], the grain size of the film after post-magnetic annealing should be larger than the case of annealing without a magnetic field. However, no such effects of magnetic annealing on the electrodeposited film were observed in our experiments, since we found that the grain size of the film annealed under a high magnetic field

In order to quantitatively analyze the effects of high magnetic fields on the roughness and the grain size of the

*m* ) and three-dimensional AFM image of the surface topography of

On the other hand, we should also take into account the effect of the magnetic field annealing on recrystallization process and grain boundary migration (GBM) in the films. If magnetic field annealing plays a retarded effect on the recrystallization process as reported by Refs. [16-17] or beneficial effects on GBM due to magnetic ordering as reported by Molodov et al [18], the grain size of the film after post-magnetic annealing should be larger than the case of annealing without a magnetic field. However, no such effects of magnetic annealing on the electrode‐ posited film were observed in our experiments, since we found that the grain size of the film annealed under a high magnetic field seemed smaller than that of the annealed film under a no-field condition.

polyhedral grains but also the grain size decreases with the disappearance of the velour-like

**(b2)**

**(b3)**

**Figure 1.** FE-SEM images of 0 T-Bed series Co/Ni film annealed under different magnetic fields (a1) 0 T, (a2) 6 T,

**Figure 1.** FE-SEM images of 0 T-Bed series Co/Ni film annealed under different magnetic fields (a1) 0 T, (a2) 6 T, (a3) 12

As it is well known, for magnetic and paramagnetic materials, magnetic field will induce a pulling force due to the magnetization [14-15], which force is favored for the separation of grains. In the meantime, an introduction of the magnetization energy during the magnetic field annealing results in the decrease of diffusion activation energy, which will improve the diffusion of the congregated deposits on the grain boundary. This is a possible reason for the grain boundary becoming clear after post-magnetic field annealing. Another most likely reason for the disappearance of velour-like product, which is estimated to be Co-oxides formed at the grain boundaries, is that the application of high magnetic fields during annealing process is favorable for the reduction of oxides, but the mechanism needs further investigation.

As it is well known, for magnetic and paramagnetic materials, magnetic field will induce a pulling force due to the magnetization [14–15], which force is favored for the separation of grains. In the meantime, an introduction of the magnetization energy during the magnetic field annealing results in the decrease of diffusion activation energy, which will improve the diffusion of the congregated deposits on the grain boundary. This is a possible reason for the grain boundary becoming clear after post-magnetic field annealing. Another most likely reason for the disappearance of velour-like product, which is estimated to be Co-oxides formed at the grain boundaries, is that the application of high magnetic fields during annealing process is favorable for the reduction of oxides, but the

On the other hand, we should also take into account the effect of the magnetic field annealing on recrystallization process and grain boundary migration (GBM) in the films. If magnetic field annealing plays a retarded effect on the recrystallization process as reported by Refs. [16–17] or beneficial effects on GBM due to magnetic ordering as reported by Molodov et al [18], the grain size of the film after post-magnetic annealing should be larger than the case of annealing without a magnetic field. However, no such effects of magnetic annealing on the electrodeposited film were observed in our experiments, since we found that the grain size of the film annealed under a high magnetic field

In order to quantitatively analyze the effects of high magnetic fields on the roughness and the grain size of the

*m* ) and three-dimensional AFM image of the surface topography of

(a3) 12 T; and 0.5 T-Bed series annealed under (b1) 0 T, (b2) 6 T, (b3) 12 T. [48]

T; and 0.5 T-Bed series annealed under (b1) 0 T, (b2) 6 T, (b3) 12 T. [48]

**(a1) (b1)**

seemed smaller than that of the annealed film under a no-field condition.

mechanism needs further investigation.

bilayered film, AFM top view ( <sup>2</sup> 1010

deposits.

262 Electroplating of Nanostructures

**(a2)**

**(a3)**

In order to quantitatively analyze the effects of high magnetic fields on the roughness and the grain size of the bilayered film, AFM top view (10×10*μm*2) and three-dimensional AFM image of the surface topography of nanocrystalline films annealed at different magnetic flux densities (Bannealing) are shown in Figure 2. The grain shape of the films is similar for the two series samples annealed under magnetic flux densities of 12 T, therefore we only provide the AFM images of 0.5 T-Bed series here. After no-field annealed, there are some ellipsoidal grains imbedded in the spherical grain matrix as seen in Figure 2 (a). While annealing in a magnetic field of 12 T, most of the grains are spherical, even some grains connect with each other to form a chain-like structure (Figure 2 (c)).

To characterize the grain size and the surface roughness, the average values were calculated using standard software (Table 1). For 0 T-Bed series, the application of 6 T magnetic field during annealing process does not affect the grain size, but leads to a decrease of surface roughness. The grain size of the films goes through minimum under the influence of a 12 T magnetic field annealing. On the other hand, in case of 0.5 T-Bed series, 6 T magnetic field annealing is enough to decrease the average grain size of the film from 140 to 100 nm.

The same magnetic annealing conditions inducing different results between the two series indicate that the influence of a weak magnetic field on the electrodeposition process can be conserved in a certain extent after post-annealing process. As the alternation of grain size during magnetic field annealing is not in a general correlation with that of surface roughness, some researchers [19] also showed that a decrease of grain size was not necessarily corre‐ sponding to a decrease in the surface roughness.

According to the results in Table 1, AFM investigations show that smaller grains and lower roughness are formed during annealing in the presence of a magnetic field comparing with the case of annealing without magnetic field. This phenomenon originates from an accelerative effect of the high magnetic fields annealing on the inter-diffusion between Co and Ni films. The initial as-deposited Co film on the surface consists of 20-50 nm sized grains, which distributed nonuniform with a large number of agglomerate as shown in Figure 3. For a given set of annealing conditions, the nanocrystalline matrix consumed by grain growth, the mean grain size continues to increase. At the meantime, inter-diffusion behavior happens between the Co and the Ni films, which results in Co atoms diffuse into the Ni matrix to form Co-Ni alloy. The application of high magnetic fields during annealing process improved the interdiffusion behavior according to the conclusions in Refs. [11] and [20]. The experimental

**Figure 2.** AFM images showing the morphology and roughness of 0.5 T-Bed series Co/Ni films annealed under different magnetic fields (a) 0 T, (b) 6 T, (c) 12 T. [48] **Figure 2.** AFM images showing the morphology and roughness of 0.5 T-Bed series Co/Ni films annealed under different magnetic fields (a) 0 T, (b) 6 T, (c) 12 T. [48]


12 T 104 ± 4 24 ± 1.6 **Table 1.** Dependence of the average grain size and the average roughness of the two series films on the magnetic **Table 1.** Dependence of the average grain size and the average roughness of the two series films on the magnetic flux density of the applied magnetic field annealing.[48]

The same magnetic annealing conditions inducing different results between the two series indicate that the influence of a weak magnetic field on the electrodeposition process can be conserved in a certain extent after post-annealing process. As the alternation of grain size during magnetic field annealing is not in a general correlation with that of surface roughness, some researchers [19] also showed that a decrease of grain size was not necessarily

According to the results in Table 1, AFM investigations show that smaller grains and lower roughness are formed during annealing in the presence of a magnetic field comparing with the case of annealing without magnetic field. This phenomenon originates from an accelerative effect of the high magnetic fields annealing on the inter-diffusion

flux density of the applied magnetic field annealing.[48]

corresponding to a decrease in the surface roughness.

evidence of this improved inter-diffusion distance by magnetic field from 920 (0 T) to 1330 nm (12 T) was obtained by XPS analysis along the cross-section of the samples. Larger volume fraction of Co-Ni nanocrystalline alloy is formed, smaller is the mean grain size. It is attributed to the crystallographic texture of Co-Ni alloy in *α*( *fcc*) phase comparing with *ε*(*hcp*) -Co, which will be discussed in detail in the next section. Another possible explanation for the results in this study is the effect of field annealing on the magnetic domains. The magnetic domains tend to be directional ordering due to magnetization under magnetic annealing, which results in the decrease of the distance between domain walls, as in turn may be responsible for the smaller grain size.

**Figure 3.** FE-SEM image of the as-deposited Co/Ni film (0 T-Bed series) before annealing.[48]

**Figure 2.** AFM images showing the morphology and roughness of 0.5 T-Bed series Co/Ni films annealed under different magnetic fields (a) 0 T, (b) 6 T, (c) 12 T. [48]

**Series Bannealing Grain size (nm) Roughness (nm)**

0 T 127 ± 5 29 ± 1.9 6 T 128 ± 3 23 ± 1.8 12 T 114 ± 3 25 ± 0.9

0 T 140 ± 6 28 ± 1.5 6 T 100 ± 3 22 ± 1.2 12 T 104 ± 4 24 ± 1.6

**Figure 2.** AFM images showing the morphology and roughness of 0.5 T-Bed series Co/Ni films annealed under different

(a)

(b)

(c)

**Table 1.** Dependence of the average grain size and the average roughness of the two series films on the magnetic

**Table 1.** Dependence of the average grain size and the average roughness of the two series films on the magnetic flux

The same magnetic annealing conditions inducing different results between the two series indicate that the influence of a weak magnetic field on the electrodeposition process can be conserved in a certain extent after post-annealing process. As the alternation of grain size during magnetic field annealing is not in a general correlation with that of surface roughness, some researchers [19] also showed that a decrease of grain size was not necessarily

According to the results in Table 1, AFM investigations show that smaller grains and lower roughness are formed during annealing in the presence of a magnetic field comparing with the case of annealing without magnetic field. This phenomenon originates from an accelerative effect of the high magnetic fields annealing on the inter-diffusion

Series Bannealing Grain size (nm) Roughness (nm)

flux density of the applied magnetic field annealing.[48]

density of the applied magnetic field annealing.[48]

magnetic fields (a) 0 T, (b) 6 T, (c) 12 T. [48]

corresponding to a decrease in the surface roughness.

0 T 127 ± 5 29 ± 1.9 6 T 128 ± 3 23 ± 1.8 12 T 114 ± 3 25 ± 0.9

0 T 140 ± 6 28 ± 1.5 6 T 100 ± 3 22 ± 1.2 12 T 104 ± 4 24 ± 1.6

0 T-Bed

0 T-Bed

264 Electroplating of Nanostructures

0.5 T-Bed

0.5 T-Bed

Figure 4 presents XRD patterns for 0.5 T-Bed series Co/Ni films in the post-magnetic annealing state with magnetic fields of 0, 6, and 12 T (Note: The 0 T-Bed series annealed under a high magnetic field show similar XRD patterns as the 0.5 T-Bed series). It can be seen that all the peaks of hcp-Co and fcc-Ni have been detected, but only one peak (220) of fcc-CoNi have been measured because of the alloying process. The diffraction peak (111) shifts to slightly higher diffraction angles in case of magnetic flux density of 6 T. One reason for the shift is most probably because of the internal stress. Some researchers [9] found the magnetic field anneal‐ ing can change the internal stress state of films. This behavior can also be rationalized as another reason: more Co atoms are incorporated into the Ni lattice under the moderate magnetic field annealing resulting in a transition from Ni-like microstructural evolution to Colike microstructural evolution [3].

Since the mean grain size *D* calculated by Scherrer's formula *<sup>D</sup>* <sup>=</sup> *<sup>k</sup><sup>λ</sup> <sup>β</sup>*cos*<sup>θ</sup>* is in inverse ratio to *β*, where *β* is the full width at half maximum (FWHM) [21]. Here, we list the width and the position of the peaks in Table 2. It can be seen from the data that the width of peaks mostly increases with the increasing magnetic flux density. This also means that the grain size decreased with the magnetic flux density. The change of grain size *D* is in the same trend as the results obtained from AFM.

Co-like microstructural evolution [3].

under the moderate magnetic field annealing resulting in a transition from Ni-like microstructural evolution to

**Figure 4.** XRD patterns of 0.5 T-Bed series Co/Ni films annealed under magnetic field of Bannealing = 0, 6, and 12 T. [48]

There is a general trend in the increase of fcc-CoNi peak (220) and the decreasing of hcp-Co peak (110) with increasing magnetic flux density during annealing process, as can be seen in the amplified zone of Figure 4 at the angular position from 2*θ* =75° to 77°. A higher volume fraction of CoNi alloy in a higher magnetic field was concluded not only from the increase of (200)CoNi compared to the (100)Co shown in Table 3 but also from the increase of diffusion zone according to the XPS composition analysis.


There is a general trend in the increase of fcc-CoNi peak (220) and the decreasing of hcp-Co peak (110) with increasing magnetic flux density during annealing process, as can be seen in the amplified zone of Figure 4 at the

concluded not only from the increase of (200)CoNi compared to the (100)Co shown in Table 3 but also from the

75 to 77 . A higher volume fraction of CoNi alloy in a higher magnetic field was

**Table 2.** The width and position of the peaks under different magnetic annealing conditions.[48] the results obtained from AFM.

increase of diffusion zone according to the XPS composition analysis.

angular position from 2


**Table 3.** The dependence of intensity (I) ratio of the three peaks on the magnetic flux density during annealing process. In the table, Value = Ifcc-CoNi /(Ifcc-CoNi + Ihcp-Co + Ifcc-Ni) × 100%.[48]

The magnetism of the films in a magnetic field is favored for the transformation of *ε*(*hcp*) structure to a more energetically stable *α*( *fcc*) structure. The application of high magnetic field annealing induces a *ε*(*hcp*)→ *α*( *fcc*) phase transformation, which may account in the increase of thermal stability of the bilayered films [22].

#### **1.4. Conclusion**

There is a general trend in the increase of fcc-CoNi peak (220) and the decreasing of hcp-Co peak (110) with increasing magnetic flux density during annealing process, as can be seen in the amplified zone of Figure 4 at the angular position from 2*θ* =75° to 77°. A higher volume fraction of CoNi alloy in a higher magnetic field was concluded not only from the increase of (200)CoNi compared to the (100)Co shown in Table 3 but also from the increase of diffusion

40 50 60 70 80 90

2 (degree)

**Figure 4.** XRD patterns of 0.5 T-Bed series Co/Ni films annealed under magnetic field of Bannealing = 0, 6, and 12 T. [48]

under the moderate magnetic field annealing resulting in a transition from Ni-like microstructural evolution to

(220)

12T 6T 0T

(110)

75 76 77

(220)

12T

6T

0T

(111) 2θ (°) 44.44 ± 0.005 44.36 ± 0.011 44.42 ± 0.014

(200) 2θ (°) 51.84 ± 0.020 51.78 ± 0.012 51.84 ± 0.011

(220) 2θ (°) 76.64 ± 0.081 76.56 ± 0.014 76.62 ± 0.024

(100) 2θ (°) 41.54 ± 0.004 41.46 ± 0.013 41.54 ± 0.007

(110) 2θ (°) 76.40 ± 0.021 76.34 ± 0.022 76.40 ± 0.007

CoNi (220) 2θ (°) 75.90 ± 0.081 75.82 ± 0.032 75.90 ± 0.006

increase of diffusion zone according to the XPS composition analysis.

**Table 2.** The width and position of the peaks under different magnetic annealing conditions.[48]

the results obtained from AFM.

angular position from 2

Since the mean grain size *D* calculated by Scherrer's formula

FWHM 0.180 ± 0.002 0.183 ± 0.005 0.182 ± 0.004

FWHM 0.157 ± 0.003 0.165 ± 0.006 0.160 ± 0.002

**Figure 4.** XRD patterns of 0.5 T-Bed series Co/Ni films annealed under magnetic field of Bannealing = 0, 6, and 12 T. [48]

the full width at half maximum (FWHM) [21]. Here, we list the width and the position of the peaks in Table 2. It can be seen from the data that the width of peaks mostly increases with the increasing magnetic flux density. This also means that the grain size decreased with the magnetic flux density. The change of grain size *D* is in the same trend as

There is a general trend in the increase of fcc-CoNi peak (220) and the decreasing of hcp-Co peak (110) with increasing magnetic flux density during annealing process, as can be seen in the amplified zone of Figure 4 at the

concluded not only from the increase of (200)CoNi compared to the (100)Co shown in Table 3 but also from the

 *<sup>k</sup> <sup>D</sup>* is in inverse ratio to

, where is

cos

75 to 77 . A higher volume fraction of CoNi alloy in a higher magnetic field was

FWHM 0.148 ± 0.008 0.161 ± 0.004 0.160 ± 0.007

FWHM 0.184 ± 0.002 0.234 ± 0.003 0.225 ± 0.009

FWHM 0.222 ± 0.008 0.261 ± 0.010 0.256 ± 0.014

FWHM 0.364 ± 0.010 0.365 ± 0.042 0.360 ± 0.029

**Bannealing (T) 0 6 12**

zone according to the XPS composition analysis.

Co-like microstructural evolution [3].

(111)

(101)

(200)

fcc-CoNi 44 45

hcp-Co fcc-Ni

(100)

Intensity (.a.u.)

(002)(111)

266 Electroplating of Nanostructures

12T 6T 0T

FCC-Ni

HCP-Co

FCC-

Uniform nanocrystalline Co/Ni bilayered films were produced by the electrodeposition assisted with a 0.5 T weak magnetic field. Magnetic fields annealing of up to 12 T were selected in this study in order to investigate the high magnetic field effects on the evolution of mor‐ phology and microstructure of the films. A 0.5 T weak magnetic field parallel to the electrode induces modification of the deposits leading to changes in the grain size during magnetic field annealing. Grain shape in the Co/Ni morphology was modified with the grain boundary becoming clearer if a high magnetic field was applied during the annealing process. Atomic force microscopy investigations show that smaller grains and lower roughness are formed during annealing in the presence of a magnetic field comparing to the case of annealing without magnetic field. With increasing magnetic flux density during annealing process, the transfor‐ mation from *ε*(*hcp*) to *α*( *fcc*) can be seen by the reduction of the *ε* -peak intensity, and the increase in that of *α* -peak. Overlapping effects of the high magnetic field annealing on diffusion, grain growth, alloying, and phase transformation have been discussed to interpret the experimental results.

**Note:** The main part, figures, and tables in **Section 1** have been published in Ref. [48].

## **2. The magnetic properties dependence on the coupled effects of magnetic fields on the microstructure of as-deposited and post-annealed Co/Ni bilayer films**

#### **2.1. Introduction**

Nano-scaled metallic multilayers received great attention in the recent years because of their unique properties, such as mechanical, optical, electrical, and magnetic, with respect to commonly used alloys. Multilayer materials can be successfully produced by electrodeposition [23], with thickness varying over a wide range from nanometric films [24-26] to micrometric coatings [27-30]. Moreover, with an accurate control of composition and thickness of each layer within the whole deposit, the internal stress that occurs usually in the microfilms can be reduced to a minimum level.

Electrodeposition is an effective method to produce cobalt-based alloys, but thin films obtained by this way contain some defects, such as rough surface. An application of parallel-toelectrode-surface magnetic field during the process can positively affect the deposits by smoothing their surfaces as well as improving magnetic properties [31-33]. This is caused by magnetohydrodynamic (MHD) and magnetocrystalline anisotropy effects. Magnetohydrody‐ namic convection induced by Lorentz force is considered as one of the characteristic phenom‐ ena in magneto-electrochemical processes [34, 35]. It is assumed that the forced convection resulting from the MHD effect decreases the thickness of the diffusion layer and enhances the concentration gradient, which improves the transport of ions toward the electrode surface. Uhlemann et al. [36] investigated the electrochemical deposition of Co-Cu/Cu multilayer under imposed magnetic field. They have reported that the deposition rate of Cu was nearly two times higher in the process carried out under magnetic field compared to the one without a Bfield. Furthermore, the authors observed also an alignment of grains in (111) direction caused by the preferred orientation of Co during the electrodeposition in an external magnetic field. In other works [37-41], the magnetic field effects on nucleation, growth, texture, phase composition, and morphology of the Co layers have been noticed. It has been shown that a magnetic field applied during the deposition process is responsible for two different effects: first, field gradients attract ferromagnetic and paramagnetic materials and repel diamagnetic ones; second, even in uniform fields, magnetic dipoles and therefore the deposits align to the magnetic field direction [42,43]. Some researchers have pointed out that when changing the magnetic field to the orientation of perpendicular-to-electrode-surface, it leads to observe some micro-MHD effects [44]. It would affect roughness and morphology of thin films, while magnetizing force could influence already mentioned magnetic properties of deposits.

It is well known that the annealing process is of a great interest due to the possibilities to decrease an internal stress and to increase the chemical order in the film. In the case of bilayered films, new phases can appear. When the annealing process is carried out under magnetic field, the material properties can be strongly modified. As an example, the Ni-Co system studied by Wang et al. [45] can be given. It was found that the annealing process caused an increase in the wear loss, which was attributed to the decrease of hardness parameter as a result of an increase in the grain size during the high-temperature treatment. Kurant et al. [46] reported a dramatic decrease of magnetic anisotropy upon annealing that was caused by an enhanced diffusion at the metals' interfaces. Harada et al. [47] observed a magnetic field effect during the annealing process on the growth of grains in nanocrystalline Ni deposit produced by the electrodeposition method. Li et al. [48] and Yu et al. [49] determined the effect of vacuum magnetic annealing of Ni and Al co-doped ZnO films on structural and physical properties. Mikelson et al. [50] obtained the aligned solidification structure in Al-Cu and Cd-Zn alloys in a 1.5 T magnetic field. Savitisky et al. [51] and Li et al. [48] found the structure alignment along the direction of magnetic field. All these experimental research works have demonstrated that a magnetic field presents significant influence on the obtained materials.

The present work investigates the Co/Ni bilayered nanocrystalline films produced through the temperature-elevated electrochemical deposition, and modified by annealing carried out also under an external magnetic field. The results indicate an increase of the coercive field of deposited Co/Ni bilayers, when the electrodeposition process was conducted under a magnetic field of 1 T. The annealing processing caused further remarkable increase of the coercive field of as-prepared bilayers that has been preserved under magnetic annealing conditions. The magnetic properties are discussed in terms of samples microstructure. In as-prepared samples the in-plane magnetization was observed, while high temperature treatment, causing micro‐ structural changes in the film, resulted also in appearance of a small component of magneti‐ zation oriented perpendicularly to the films' plane that could have been observed by MFM analysis. The induced perpendicular magnetization component in the post-annealed samples was a result of the magnetic field applied in the perpendicular direction to the samples' surface during annealing treatment.

#### **2.2. Experimental methodology**

[23], with thickness varying over a wide range from nanometric films [24-26] to micrometric coatings [27-30]. Moreover, with an accurate control of composition and thickness of each layer within the whole deposit, the internal stress that occurs usually in the microfilms can be

Electrodeposition is an effective method to produce cobalt-based alloys, but thin films obtained by this way contain some defects, such as rough surface. An application of parallel-toelectrode-surface magnetic field during the process can positively affect the deposits by smoothing their surfaces as well as improving magnetic properties [31-33]. This is caused by magnetohydrodynamic (MHD) and magnetocrystalline anisotropy effects. Magnetohydrody‐ namic convection induced by Lorentz force is considered as one of the characteristic phenom‐ ena in magneto-electrochemical processes [34, 35]. It is assumed that the forced convection resulting from the MHD effect decreases the thickness of the diffusion layer and enhances the concentration gradient, which improves the transport of ions toward the electrode surface. Uhlemann et al. [36] investigated the electrochemical deposition of Co-Cu/Cu multilayer under imposed magnetic field. They have reported that the deposition rate of Cu was nearly two times higher in the process carried out under magnetic field compared to the one without a Bfield. Furthermore, the authors observed also an alignment of grains in (111) direction caused by the preferred orientation of Co during the electrodeposition in an external magnetic field. In other works [37-41], the magnetic field effects on nucleation, growth, texture, phase composition, and morphology of the Co layers have been noticed. It has been shown that a magnetic field applied during the deposition process is responsible for two different effects: first, field gradients attract ferromagnetic and paramagnetic materials and repel diamagnetic ones; second, even in uniform fields, magnetic dipoles and therefore the deposits align to the magnetic field direction [42,43]. Some researchers have pointed out that when changing the magnetic field to the orientation of perpendicular-to-electrode-surface, it leads to observe some micro-MHD effects [44]. It would affect roughness and morphology of thin films, while magnetizing force could influence already mentioned magnetic properties of deposits.

It is well known that the annealing process is of a great interest due to the possibilities to decrease an internal stress and to increase the chemical order in the film. In the case of bilayered films, new phases can appear. When the annealing process is carried out under magnetic field, the material properties can be strongly modified. As an example, the Ni-Co system studied by Wang et al. [45] can be given. It was found that the annealing process caused an increase in the wear loss, which was attributed to the decrease of hardness parameter as a result of an increase in the grain size during the high-temperature treatment. Kurant et al. [46] reported a dramatic decrease of magnetic anisotropy upon annealing that was caused by an enhanced diffusion at the metals' interfaces. Harada et al. [47] observed a magnetic field effect during the annealing process on the growth of grains in nanocrystalline Ni deposit produced by the electrodeposition method. Li et al. [48] and Yu et al. [49] determined the effect of vacuum magnetic annealing of Ni and Al co-doped ZnO films on structural and physical properties. Mikelson et al. [50] obtained the aligned solidification structure in Al-Cu and Cd-Zn alloys in a 1.5 T magnetic field. Savitisky et al. [51] and Li et al. [48] found the structure alignment along the direction of magnetic field. All these experimental research works have demonstrated that

a magnetic field presents significant influence on the obtained materials.

reduced to a minimum level.

268 Electroplating of Nanostructures

The electrochemical experiments were performed in a conventional three-electrode cell. The working electrode (WE) was a square glass substrate of dimensions of 10 × 10 mm and 1.1 mm height, covered with ITO (In2O3:SnO2) coating (electric contact layer) and embedded into a cylindrical holder. The counter electrode was made of a platinum plate and the reference electrode was a saturated mercury sulfate electrode (SSE). Electrodeposition process has been carried out in a cylindrical double-wall cell under the conditions listed in Table 4. The electrochemical cell was plunged into the gap of Drusch EAM 20G electromagnet, which delivers a uniform horizontal magnetic field parallel or perpendicular to the electrode surface.


**Table 4.** Processing conditions for the Co/Ni bilayer thin films. [56]

The electrodeposition process included two steps, which were related to: firstly - deposition of Ni seed-layer directly on ITO/glass substrate, secondly - deposition of Co layer. The Ni seedlayer deposition was undertaken without an applied magnetic field, while the Co layers deposition was performed under superimposition of a magnetic field with the strength up to 1 T in parallel-to-electrode-surface orientation. Thicknesses of the layers were determined according to the X-Ray photoelectron spectroscopy (XPS) measurements done for the similar, but thicker than considered here, Co/Ni layers reported in Ref. [52]. The difference between these two investigated systems is the deposition time, which in [52] was longer: 6 min deposition of Ni seed layer and 4 min deposition of Co proper layer, respectively. Thus, based on this the estimated thickness of layers considered in this work is approximately 200 nm for Ni and 300-400 nm for Co layer, depending on the magnetic field intensity. Additionally, the roughness of Ni seed-layer determined by AFM was 40 ± 3*nm*, while the roughness of Co secondary layer was 38 ± 2*nm* when the process was carried out without a superimposed magnetic field. Then, roughness of the Co layer has been slightly improved (decreased) when electrodeposition was carried out under superimposed magnetic field: ~ 35 nm (±3) and 29 nm (±2) under 0.5 and 1 T, respectively. The electrolyte pH was adjusted to proper level by addition of sulfuric acid or sodium hydroxide. Besides the basic salts no other chemical additives, which are usually used to avoid the effect of hydrogen evolution on the films morphology, were added. Boric acid, in addition to its buffer function, is a useful additive compound favoring the formation of low roughness deposits. All of the electrochemical investigations were carried out using the chronopotentiometry method, where a constant current density of -10 mA/cm2 was applied. The potential of working electrode was controlled by means of a potentiostatgalvanostat VersaSTAT4. The heat treatment process of Co/Ni bilayered films was carried out in a vertical furnace placed into the superconducting magnet with strength up to 12 T and perpendicular magnetic field flux to the samples surface. The films were annealed at 673 K during 4 h under a protective atmosphere of high-purity argon and then cooled down to the room temperature. Bruker D8 Advance and GI-XRD Ultima IV X-ray Diffractometers with CuKα radiation have been employed to obtain XRD patterns using standard θ-2θ geometry. Microstructures of the obtained layers have been investigated by field emission scanning electron microscopy (FE-SEM) Supra 35, Japan. The hysteresis loops have been measured by means of a vector VSM (LakeShore 7410) and an alternating gradient field magnetometer (AGFM, PMC 2900) and the magnetic field has been applied in the in-plane configuration. Magnetic force microscopy (MFM, Bruker Multimode V Nanoscope 8) analysis has been performed in tapping-lift mode with CoCr-coated tips.

#### **2.3. Results and discussion**

In order to determine the effects of magnetic fields superimposed during both electrodeposi‐ tion and annealing processes on the magnetic properties of Co/Ni/ITO bilayer films, room temperature in-plane hysteresis loops were recorded. Figure 5 indicates the magnetic charac‐ teristic of as-prepared Co/Ni/ITO films.

It is observed that film deposited under 1 T magnetic field tends to be slightly more difficult to magnetize than film deposited in the absence of an external magnetic field. An increase in coercivity (Hc), from 45 Oe (As-deposited, 0 T) to 78 Oe (As-deposited, 1 T) is noticed, when a magnetic field was superimposed during electrodeposition. The occurred variation in the coercive field cannot be attributed to induced magneto-crystalline anisotropy, as is usually the case in physical deposition processes under the application of a magnetic field. In fact, no significant dependence of the magnetic properties is observed along different directions of the

according to the X-Ray photoelectron spectroscopy (XPS) measurements done for the similar, but thicker than considered here, Co/Ni layers reported in Ref. [52]. The difference between these two investigated systems is the deposition time, which in [52] was longer: 6 min deposition of Ni seed layer and 4 min deposition of Co proper layer, respectively. Thus, based on this the estimated thickness of layers considered in this work is approximately 200 nm for Ni and 300-400 nm for Co layer, depending on the magnetic field intensity. Additionally, the roughness of Ni seed-layer determined by AFM was 40 ± 3*nm*, while the roughness of Co secondary layer was 38 ± 2*nm* when the process was carried out without a superimposed magnetic field. Then, roughness of the Co layer has been slightly improved (decreased) when electrodeposition was carried out under superimposed magnetic field: ~ 35 nm (±3) and 29 nm (±2) under 0.5 and 1 T, respectively. The electrolyte pH was adjusted to proper level by addition of sulfuric acid or sodium hydroxide. Besides the basic salts no other chemical additives, which are usually used to avoid the effect of hydrogen evolution on the films morphology, were added. Boric acid, in addition to its buffer function, is a useful additive compound favoring the formation of low roughness deposits. All of the electrochemical investigations were carried out using the chronopotentiometry method, where a constant current density of -10 mA/cm2 was applied. The potential of working electrode was controlled by means of a potentiostatgalvanostat VersaSTAT4. The heat treatment process of Co/Ni bilayered films was carried out in a vertical furnace placed into the superconducting magnet with strength up to 12 T and perpendicular magnetic field flux to the samples surface. The films were annealed at 673 K during 4 h under a protective atmosphere of high-purity argon and then cooled down to the room temperature. Bruker D8 Advance and GI-XRD Ultima IV X-ray Diffractometers with CuKα radiation have been employed to obtain XRD patterns using standard θ-2θ geometry. Microstructures of the obtained layers have been investigated by field emission scanning electron microscopy (FE-SEM) Supra 35, Japan. The hysteresis loops have been measured by means of a vector VSM (LakeShore 7410) and an alternating gradient field magnetometer (AGFM, PMC 2900) and the magnetic field has been applied in the in-plane configuration. Magnetic force microscopy (MFM, Bruker Multimode V Nanoscope 8) analysis has been

In order to determine the effects of magnetic fields superimposed during both electrodeposi‐ tion and annealing processes on the magnetic properties of Co/Ni/ITO bilayer films, room temperature in-plane hysteresis loops were recorded. Figure 5 indicates the magnetic charac‐

It is observed that film deposited under 1 T magnetic field tends to be slightly more difficult to magnetize than film deposited in the absence of an external magnetic field. An increase in coercivity (Hc), from 45 Oe (As-deposited, 0 T) to 78 Oe (As-deposited, 1 T) is noticed, when a magnetic field was superimposed during electrodeposition. The occurred variation in the coercive field cannot be attributed to induced magneto-crystalline anisotropy, as is usually the case in physical deposition processes under the application of a magnetic field. In fact, no significant dependence of the magnetic properties is observed along different directions of the

performed in tapping-lift mode with CoCr-coated tips.

**2.3. Results and discussion**

270 Electroplating of Nanostructures

teristic of as-prepared Co/Ni/ITO films.

**Figure 5.** Comparison of the hysteresis loops of Co/Ni/ITO bilayer films electrodeposited without and with a superim‐ posed magnetic field.[56]

applied magnetic field, in the sample plane. Instead, electrochemical deposition under magnetic field affects locally the chemical environment surrounding the magnetic atoms and the mechanisms of grain growth; therefore, the increased value of Hc might be explained in terms of a possible variation of the shape anisotropy of the Co crystals, as reported in [53], or to a slightly larger crystal size when deposition occurs under an applied magnetic field. One of the key issues for the dependence of coercivity on the grain size is the domains around grain boundaries. The rearrangement of the domains costs some energy and therefore contributes to coercivity [54]. The relative volume of the grain boundary domains increases with the increasing of the magnetocrystalline anisotropy, consequently leading to a rise in coercivity.

Both samples were then annealed under magnetic conditions and the hysteresis loops were again recorded. In both cases, as-deposited Co/Ni/ITO films under 0 and 1 T magnetic field, a significant increase of the coercive fields was observed. At the same time, a slower approach to the saturation has been noticed, which is probably due to the increased intermixing of Co and Ni atoms at the interfaces, since their existence has been proven and discussed in Ref. [54]. An increased Hc is mostly associated with the mixed effects of recrystallization process and structural modifications. Further annealing under magnetic conditions of 6 and 12 T brings about only a slight increase of the Hc value (Figure 6), which is most likely to be caused by enhanced increase of Co grains and structural directionality. However, the presence of an interdiffusion zone between Co and Ni layers cannot be neglected as well. In any case, no significant induced magnetocrystalline anisotropy seems to come from the field annealing procedure, as the final coercivity values are mostly independent of the application of a magnetic field during annealing.

**Figure 6.** Comparison of the coercivity field of Co/Ni/ITO bilayer films before (as-deposited) and after (post-annealed) annealing treatment.[56]

Extended analysis of the magnetic characteristics of post-annealed Co/Ni/ITO bilayer films have been done by use of magnetic force microscopy (MFM). All samples have been investi‐ gated at their in-plane remanence, after a saturating magnetic field has been applied. The MFM tip is magnetized perpendicular to the sample plane; therefore, the MFM is sensitive to the second derivative of the *z* component of the field generated by the sample magnetization in the half space above the sample surface. The images report in false colors the phase channel in pass 2 (retrace) at a lift scan height of 50 nm. Figure 7 presents MFM images of the Co/Ni/ITO films as-deposited and post-annealed, respectively, on the base of AFM images presented in Figure 2. The magnetic structure consists of bubble-like domains - small, cylin‐ drical magnetic domains that are usually formed when an external magnetic field is applied perpendicularly to the surface of the film. In general, the domains run in random directions in the film plane, i.e., no directionality in the orientation of domains is observed. The domains are displayed as bright and dark areas and have opposite magnetization components perpen‐ dicular to the film surface. For the sample deposited under no magnetic field, annealing is responsible for a severe change of the domain structure that is not significantly affected by the application of a magnetic field, in agreement with the coercivity values reported in Figure 6. In particular, the magnetic features size considerably reduces with respect to the as-deposited film, whereas the increased magnetic contrast (as documented by the very different color scales in the top row images in Figure 7) can be attributed to a stronger anisotropy within the individual grains, in turn responsible for the increase of Hc. The Co/Ni films' exposure on the high-temperature treatment changes their microstructure in means of grains' growth. Under thermal conditions, the grains of as-deposited films that were mostly agglomerated into islands begin to grow separately due to the broken symmetry at the interfaces. As a result, ultra-thin magnetic layers tend to be perpendicularly magnetized. Additional contribution might also come from dipolar interaction between the grain islands in the film. In consequence, the observed increasing anisotropy is a result of the single grains growth that boundaries become more clear and visible, and thus, the increased magnetic contrast is observed.

significant induced magnetocrystalline anisotropy seems to come from the field annealing procedure, as the final coercivity values are mostly independent of the application of a

**Figure 6.** Comparison of the coercivity field of Co/Ni/ITO bilayer films before (as-deposited) and after (post-annealed)

Extended analysis of the magnetic characteristics of post-annealed Co/Ni/ITO bilayer films have been done by use of magnetic force microscopy (MFM). All samples have been investi‐ gated at their in-plane remanence, after a saturating magnetic field has been applied. The MFM tip is magnetized perpendicular to the sample plane; therefore, the MFM is sensitive to the second derivative of the *z* component of the field generated by the sample magnetization in the half space above the sample surface. The images report in false colors the phase channel in pass 2 (retrace) at a lift scan height of 50 nm. Figure 7 presents MFM images of the Co/Ni/ITO films as-deposited and post-annealed, respectively, on the base of AFM images presented in Figure 2. The magnetic structure consists of bubble-like domains - small, cylin‐ drical magnetic domains that are usually formed when an external magnetic field is applied perpendicularly to the surface of the film. In general, the domains run in random directions in the film plane, i.e., no directionality in the orientation of domains is observed. The domains are displayed as bright and dark areas and have opposite magnetization components perpen‐

magnetic field during annealing.

272 Electroplating of Nanostructures

annealing treatment.[56]

No preferred orientation of the anisotropy is observed even under the application of a 12 T field during annealing. For the sample deposited under the application of a 1 T field on the sample plane, the magnetic features in the as-prepared state are very different with respect to the sample deposited in 0 field, because of the different grain growth mechanisms.

**Figure 7.** MFM analysis of the Co/Ni/ITO films. The lateral size of each image is 5 μm.[56]

However, after annealing a domain configuration similar to the other sample is obtained, again with no significant dependence on the field intensity applied during annealing. The slightly reduced color scale in the images of the bottom row of Figure 7 with respect to those of the top row account for a slightly lower anisotropy value of the Co grains, which is in agreement with the slightly lower coercivity reported in Figure 6. Moreover, a 2D power spectral density [55] calculated on the MFM images of Figure 7 reports a slight decrease of the magnetic features size after annealing, as evidenced in Figure 8 for two examples, as-prepared sample and annealed at 6 T.

**Figure 8.** 2D power spectral density of the as-prepared and post-annealed Co/Ni/ITO films.[56]

The appearance of a maximum in the blue curve at higher frequencies (shorter wavelengths) marks the decrease of magnetic features size that can be attributed to a slight increase of the magnetic anisotropy with annealing; a similar behavior has been observed in L10 Fe-Pt films [55]. This is in agreement with the measured hysteresis loops, as discussed in Figures 5 and 6. The observed magnetic anisotropy is probably due to the magnetic interactions among the grains: in fact, MFM images (Figure 7) reveal that the magnetic features are larger than the individual grains (AFM images, Figure 2); an increase of the grain size as a consequence of the annealing process increases the dipolar coupling energy among the grains: they are no longer agglomerated into island, but grow separately with larger volume of grain boundaries that results in easier magnetic interaction between them.

In consequence, increasing effective magnetic anisotropy is observed, in agreement with Figure 7, where most grains have preferred orientations in the presence of an external magnetic field. Thus, the magnetic domain structure determines the hysteresis loops of Co/Ni/ITO films, and the domains configuration is affected by the surface morphology, while their reduced size is probably affected by structural defects, such as grain boundaries and impurities.

## **2.4. Conclusion**

the slightly lower coercivity reported in Figure 6. Moreover, a 2D power spectral density [55] calculated on the MFM images of Figure 7 reports a slight decrease of the magnetic features size after annealing, as evidenced in Figure 8 for two examples, as-prepared sample and

**Figure 8.** 2D power spectral density of the as-prepared and post-annealed Co/Ni/ITO films.[56]

results in easier magnetic interaction between them.

The appearance of a maximum in the blue curve at higher frequencies (shorter wavelengths) marks the decrease of magnetic features size that can be attributed to a slight increase of the magnetic anisotropy with annealing; a similar behavior has been observed in L10 Fe-Pt films [55]. This is in agreement with the measured hysteresis loops, as discussed in Figures 5 and 6. The observed magnetic anisotropy is probably due to the magnetic interactions among the grains: in fact, MFM images (Figure 7) reveal that the magnetic features are larger than the individual grains (AFM images, Figure 2); an increase of the grain size as a consequence of the annealing process increases the dipolar coupling energy among the grains: they are no longer agglomerated into island, but grow separately with larger volume of grain boundaries that

In consequence, increasing effective magnetic anisotropy is observed, in agreement with Figure 7, where most grains have preferred orientations in the presence of an external magnetic field. Thus, the magnetic domain structure determines the hysteresis loops of Co/Ni/ITO films,

annealed at 6 T.

274 Electroplating of Nanostructures

The coupled effects of a superimposed magnetic field during both electrodeposition and magnetic annealing treatment in dependence on Co/Ni/ITO microstructure were investigated. The magnetic fields applied in the two processes (growth and annealing) play very different roles. During growth, the modified electrochemical environment around the electrode is responsible for the deposition of Co atoms in islands having a different size and shape anisotropies that result in a higher coercivity. Conversely, it has been shown that the crystal‐ lographical structure of as-deposited films is improved by annealing treatment that induces the recrystallization effect. A superimposed magnetic field during annealing promotes diffusion of atoms between Co and Ni layers. The magnetic field annealing has affected the magnetic properties of Co/Ni/ITO films by minimizing the magnetic anisotropy energy of the systems due to the stress relief between grains and directional atomic pair ordering. The direction bonds of dissimilar atoms (Co, Ni) in the films may affect their asymmetric distri‐ bution under superimposed magnetic field, when supposing that its strength is sufficiently high. Furthermore, the magnetic field annealing increases the dipolar interactions between metals grains and the redistribution of pair ordering directions, which are perpendicular to the magnetization direction in each domain, as in the case of Co/Ni/ITO films, can be observed. An increased magnetic anisotropy in the investigated films was always obtained after annealing, with coercive fields up to about 100 Oe.

**Note:** The main part, figures, and tables in **Section 2** have been published in Ref. [56].

## **3. Influence of high magnetic field annealing on the microstructure of pulse-electrodeposited nanocrystalline Co-Ni-P films**

#### **3.1. Introduction**

The electrodeposited Co-Ni-P film is a promising magnetic material for micro-electromechanical systems (MEMS) [57] and magnetic recording media [58]. The alloy film prepara‐ tion by pulse electrodeposition method [59] presents the advantage of a nanocrystalline regime and a fine magnetic property, with a low production cost. However, the nonequilibrium state of the as-electrodeposited nanocrystalline layers, in another word, the strong thermodynamic potential for grain growth, may be a limiting factor in the successful applications of this functional film. Recently, the possibility of controlling the grain growth and improving the thermal stability in the as-deposited films by using magnetic field annealing was reported [60 - 62]. Harada et al. [63] annealed the electrodeposited nanocrystalline Ni under a 1.2 MA/ m field and found grain growth could not occur after the early stage. Few applications of high magnetic field during annealing process [64] prove it a promising method to tailor the final microstructure (e.g., surface topography, grain size, crystallographic orientation). In this work, we focus on the microstructure evolution of pulsed-electrodeposited Co-Ni-P film during the magnetic annealing process.

## **3.2. Experimental**

The bath (pH = 3.7) for the electrodeposition of CoNiP films consisted of 0.91 M NiSO4 6H2O, 0.17 M NiCl2 6H2O, 0.11 M CoSO4 7H2O, 0.48 M H3BO3, 0.29 M NaH2PO2, and 0.0035 M C12H25NaO4S. All electrochemical experiments were performed in a conventional twoelectrode cell without agitation. The cathode was Cu plate (10 × 10 × 1 mm) with a seed layer Ni (~60 nm), which was prepared by the physical vacuumed deposition (PVD) method. A nickel plate with area of 2 cm2 was used as the anode. A unidirectional rectangle pulse current was used, the current was 0.01 A and the duty ratio was 1:5. The pulse-electrodeposition was performed at room temperature for 30 min. After electrodeposited, the samples were heattreated at 673 K for 4 h under a protective atmosphere of high-purity argon in a vertical furnace, which was placed inside a superconducting magnet. The direction of the external magnetic field was in perpendicular to the surface of the films, and the applied magnetic flux density (B) during the annealing process was up to 9 T. Surface morphology of the Co-Ni-P alloy thin films were observed by field emission scanning electronic microscopy (FE-SEM, SUPRA 35, German). To quantitatively analyze the grain size and the roughness of the films, atomic force microscopy (AFM, NTEGRA AURA, NT-MDT, Russia) was used in the area of 15×15 *μm* at three different positions to obtain average data. The crystal structure was detected by grazing incidence X-ray diffraction (GI-XRD, Ultima IV, Japan) using Cu *Kα<sup>1</sup>* radiation (40 kV, 40 mA, 0.02°/step).

#### **3.3. Results and Discussion**

#### *3.3.1. Surface morphology*

In Figure 9, surface morphologies of the as-deposited Co-Ni-P film and the annealed films with and without high magnetic field were observed by FE-SEM. It was apparent that the annealing process, whether with or without a magnetic field, induced an obvious evolution in the morphology of the as-electrodeposited film. The as-deposited Co-Ni-P film (Figure 9 (a)) shows a kind of grape-like structure that combined of spherical clusters with different sizes, meanwhile, the surface of the as-deposited film was rough and inhomogeneous. After annealed at 673 K, the small grains in the clusters coalesced together to form bigger grains, with the small grains vanishing at the edges of the bigger grains due to a recrystallization process. However, a 9 T magnetic field annealing favored to form a more uniform surface with smaller grain size and lower roughness, compared with the annealed samples obtained in the absence of magnetic field. The white dots in Figure 9 (b) were phosphorus grains separated out from the alloy, which dots disappeared when a 9 T magnetic field was applied during annealing process. The influencing mechanisms of high magnetic field annealing on the morphology evolution in the CoNiP electrodeposits can be interpreted in terms of the overlapping effects: diffusion and recrystallization. On one side, the introduction of the magnetization energy during the magnetic field annealing decreased the diffusion activation energy [65], resulting in an acceleration effect on diffusion. On the other side, owing to the fact that the retarded effect of a 9 T strong magnetic field on the recrystallization process plays a more important role against its acceleration effect on diffusion process [66-67], the coalescence and growth of small grains were suppressed. during the annealing process was up to 9 T. Surface morphology of the Co-Ni-P alloy thin films were observed by field emission scanning electronic microscopy (FE-SEM, SUPRA 35,German). To quantitatively analyze the grain size and the roughness of the films, atomic force microscopy (AFM, NTEGRA AURA, NT-MDT, Russia) was used in the area of 15×15 *m*at three different positions to obtain average data. The crystal structure was detected by

grazing incidence X-ray diffraction (GI-XRD, Ultima IV, Japan) using Cu *Kα1* radiation (40 kV, 40 mA, 0.02°/step).

**Figure 9.** Typical FE-SEM images of as deposited CoNiP thin film (a) and post-annealed in the case of: (b) B = 0 T, (c) B = 9 T. **Figure 9.** Typical FE-SEM images of as deposited CoNiP thin film (a) and post-annealed in the case of: (b) B = 0 T, (c) B = 9 T.

#### In Figure 9., surface morphologies of the as-deposited Co-Ni-P film and the annealed films with and without high magnetic field were observed by FE-SEM. It was apparent that the annealing process, whether with or without a *3.3.2. Average grain size and roughness*

microstructure (e.g., surface topography, grain size, crystallographic orientation). In this work, we focus on the microstructure evolution of pulsed-electrodeposited Co-Ni-P film during the

The bath (pH = 3.7) for the electrodeposition of CoNiP films consisted of 0.91 M NiSO4 6H2O, 0.17 M NiCl2 6H2O, 0.11 M CoSO4 7H2O, 0.48 M H3BO3, 0.29 M NaH2PO2, and 0.0035 M C12H25NaO4S. All electrochemical experiments were performed in a conventional twoelectrode cell without agitation. The cathode was Cu plate (10 × 10 × 1 mm) with a seed layer Ni (~60 nm), which was prepared by the physical vacuumed deposition (PVD) method. A

was used, the current was 0.01 A and the duty ratio was 1:5. The pulse-electrodeposition was performed at room temperature for 30 min. After electrodeposited, the samples were heattreated at 673 K for 4 h under a protective atmosphere of high-purity argon in a vertical furnace, which was placed inside a superconducting magnet. The direction of the external magnetic field was in perpendicular to the surface of the films, and the applied magnetic flux density (B) during the annealing process was up to 9 T. Surface morphology of the Co-Ni-P alloy thin films were observed by field emission scanning electronic microscopy (FE-SEM, SUPRA 35, German). To quantitatively analyze the grain size and the roughness of the films, atomic force microscopy (AFM, NTEGRA AURA, NT-MDT, Russia) was used in the area of 15×15 *μm* at three different positions to obtain average data. The crystal structure was detected by grazing incidence X-ray diffraction (GI-XRD, Ultima IV, Japan) using Cu *Kα<sup>1</sup>* radiation (40 kV, 40 mA,

In Figure 9, surface morphologies of the as-deposited Co-Ni-P film and the annealed films with and without high magnetic field were observed by FE-SEM. It was apparent that the annealing process, whether with or without a magnetic field, induced an obvious evolution in the morphology of the as-electrodeposited film. The as-deposited Co-Ni-P film (Figure 9 (a)) shows a kind of grape-like structure that combined of spherical clusters with different sizes, meanwhile, the surface of the as-deposited film was rough and inhomogeneous. After annealed at 673 K, the small grains in the clusters coalesced together to form bigger grains, with the small grains vanishing at the edges of the bigger grains due to a recrystallization process. However, a 9 T magnetic field annealing favored to form a more uniform surface with smaller grain size and lower roughness, compared with the annealed samples obtained in the absence of magnetic field. The white dots in Figure 9 (b) were phosphorus grains separated out from the alloy, which dots disappeared when a 9 T magnetic field was applied during annealing process. The influencing mechanisms of high magnetic field annealing on the morphology evolution in the CoNiP electrodeposits can be interpreted in terms of the overlapping effects: diffusion and recrystallization. On one side, the introduction of the

was used as the anode. A unidirectional rectangle pulse current

magnetic annealing process.

nickel plate with area of 2 cm2

**3.3. Results and Discussion**

*3.3.1. Surface morphology*

**3.2. Experimental**

276 Electroplating of Nanostructures

0.02°/step).

magnetic field, induced an obvious evolution in the morphology of the as-electrodeposited film. The as-deposited Co-Ni-P film (Figure 9 (a)) shows a kind of grape-like structure that combined of spherical clusters with different sizes, meanwhile, the surface of the as-deposited film was rough and inhomogeneous. After annealed at 673 K, the small grains in the clusters coalesced together to form bigger grains, with the small grains vanishing at the edges of the bigger grains due to a recrystallization process. However, a 9 T magnetic field annealing favored to form a more uniform surface with smaller grain size and lower roughness, compared with the annealed samples obtained in the absence of magnetic field. The white dots in Figure 9 (b) were phosphorus grains separated out from the alloy, which dots disappeared when a 9 T magnetic field was applied during annealing process. The influencing mechanisms of high magnetic field annealing on the morphology evolution in the CoNiP electrodeposits can be interpreted in terms of the overlapping effects: diffusion and recrystallization. On one side, the introduction of the magnetization energy during the magnetic field annealing decreased the diffusion activation energy [65], resulting in an acceleration effect on diffusion. On the other side, owing to the fact that the retarded effect of a 9 T strong magnetic field on the recrystallization process plays a more important role against its acceleration effect on diffusion process [66–67], the coalescence and growth of small grains were suppressed. **3.3.2 Average grain size and roughness** In order to quantitatively analyze the roughness and the grain size of the CoNiP films, AFM top view and In order to quantitatively analyze the roughness and the grain size of the CoNiP films, AFM top view and three-dimensional image of the nanocrystalline films, before annealed, and annealed at different magnetic flux densities (0 T, 9 T) are shown in Figure 10. On the surface of all the films, most grains were in spherical shape with crack-free. Comparing with the asdeposited film, the grain size and roughness in the case of no-field annealing increased dramatically. While the application of 9 T magnetic field during annealing process leads to a decrease in grain size and surface roughness. The average grain size and the average roughness were calculated by standard Nova software attached on the AFM setup. According to the values in Table 5, it was obvious that no significant increase in the grain size of the film after annealed at 9 T field (around 44 nm) in comparison with the as-deposited sample was observed, only a little bigger than that of the as-deposited film (around 32 nm). The evolution of roughness was in the same tendency with that of grain size. Therefore, there is no doubt that a high magnetic field, which plays an important role on grain growth, diffusion, and recrystallization, can be applied to control the grain growth of an as-electrodeposited film during annealing process for improving its thermal stability.


Nova software attached on the AFM setup. According to the values in Table 5, it was obvious that no significant increase in the grain size of the film after annealed at 9 T field (around 44 nm) in comparison with the as-deposited sample was observed, only a little bigger than that of the as-deposited film (around 32 nm). The evolution of **Table 5.** Grain size and roughness of the CoNiP films, before annealed and post-annealed under a 0 T or 9 T magnetic field.

roughness was in the same tendency with that of grain size. Therefore, there is no doubt that a high magnetic field, which plays an important role on grain growth, diffusion, and recrystallization, can be applied to control the grain

growth of an as-electrodeposited film during annealing process for improving its thermal stability.

**(a)As deposited (b)B=0T (c)B=9T**

**Figure 10.** Typical AFM images of CoNiP films, (a) as-deposited and post-annealed under field of 0 T (b) and 9 T (c). magnetic field.

**Figure 10.** Typical AFM images of CoNiP films, (a) as-deposited and post-annealed under field of 0 T (b) and 9 T (c).

#### *3.3.3. Crystal structure* **3.3.3 Crystal structure**

**3.4 Conclusion** 

**As deposited Annealed 0T Annealed 9T(**ⅲ**)** Grain size (nm) 32.2±3.4 97.53±5.5 44.6±2.6 The XRD patterns of as deposited and post-annealed samples were shown in Figure 11. The magnified diffraction pattern between 42° and 48° of 2θ is shown in the inset of (A). The XRD patterns of as deposited and post-annealed samples were shown in Figure 11. The magnified diffraction pattern between 42° and 48° of 2θ is shown in the inset of (A).

(002)Intensity (a.u.)(200)(220)B=9T (100)42 44 46 48 **Figure 11.** XRD patterns of as-deposited CoNiP film (a), and post-annealed under the magnetic field of : (b) B = 0 T; (c) B = 9 T. A magnified diffraction pattern between 42° and 48° is shown in the inset of (A). **Figure 11.** XRD patterns of as-deposited CoNiP film (a), and post-annealed under the magnetic field of : (b) B = 0 T; (c) B = 9 T. A magnified diffraction pattern between 42° and 48° is shown in the inset of (A).

40 50 60 70 80 90 2 (degrees) B=0T As deposited The as-deposited CoNiP film showed a kind of fcc structure which was the *α*-phase of the Co-based alloy. After annealed at 673 K, an additional hcp-Co (002) peak around 45° appeared, since according to the research of Lew et al. [68]the <001> texture will form after annealed. In the case of annealed under field of 9 T, the (111) diffraction peak of fcc-Ni and the (100) peak of hcp-Co were measured. This means a high magnetic field induces a mixed structure in the film that consists of fcc-Ni, hcp-Co together with fcc-CoNiP alloy. In addition, the diffraction peak The as-deposited CoNiP film showed a kind of fcc structure which was the *α*-phase of the Cobased alloy. After annealed at 673 K, an additional hcp-Co (002) peak around 45° appeared, since according to the research of Lew et al. [68] the <001> texture will form after annealed. In the case of annealed under field of 9 T, the (111) diffraction peak of fcc-Ni and the (100) peak of hcp-Co were measured. This means a high magnetic field induces a mixed structure in the film that consists of fcc-Ni, hcp-Co together with fcc-CoNiP alloy. In addition, the diffraction peak (111) of *α*-phase shifts to lower diffraction angles in case of magnetic flux density of 9 T.

**Figure 11.** XRD patterns of as-deposited CoNiP film (a), and post-annealed under the magnetic field of : (b) B = 0 T; (c) B = 9 T. A magnified diffraction pattern between 42° and 48° is shown in the inset of (A).

The as-deposited CoNiP film showed a kind of fcc structure which was the *α*-phase of the Co-based alloy. After annealed at 673 K, an additional hcp-Co (002) peak around 45° appeared, since according to the research of Lew et al. [68] the <001> texture will form after annealed. In the case of annealed under field of 9 T, the (111) diffraction

We have studied the influence of high magnetic eld annealing on the grain growth and phase structure of pulse electrodeposition CoNiP films. FE-SEM and AFM studies showed that the grains size and the roughness were decreased after annealed under the high magnetic field. X-ray diffraction patterns showed that a mixed phase

**Note 1:** The main part, figures, and tables in **Section 3** have been published on Journal of Iron and Steel

magnetic field annealing on microstructure of pulse-electrodeposited nanocrystalline Co-Ni-P films. J

high magnetic field on diffusion modifies this tendency during the annealing process.

structure was formed in the annealed film under a 9 T magnetic field.

Research as: Li DG, Chun WU, Qiang W, Agnieszka F, He J-C. Influence of high

(111) of *α*-phase shifts to lower diffraction angles in case of magnetic flux density of 9 T. This behavior can be rationalized as more Ni atoms are separated out of the CoNiP solid solution under a high magnetic field, resulting in a transition from Ni-like fcc-microstructural evolution to Co-like fcc-microstructural [69]. The XRD results reveal that during the electrodeposition process, the structure of supersaturated solid solution CoNiP (*α*-phase), is not stable. After annealing, Ni and Co atoms have a potential to separate out of the alloy, and an accelerating effect of This behavior can be rationalized as more Ni atoms are separated out of the CoNiP solid solution under a high magnetic field, resulting in a transition from Ni-like fcc-microstructural evolution to Co-like fcc-microstructural [69]. The XRD results reveal that during the electro‐ deposition process, the structure of supersaturated solid solution CoNiP (*α*-phase), is not stable. After annealing, Ni and Co atoms have a potential to separate out of the alloy, and an accelerating effect of high magnetic field on diffusion modifies this tendency during the annealing process.

## **3.4. Conclusion**

**Figure 10.** Typical AFM images of CoNiP films, (a) as-deposited and post-annealed under field of 0 T (b) and 9 T (c).

**Table 5.** Grain size and roughness of the CoNiP films, before annealed and post-annealed under a 0 T or 9 T magnetic field.

**Figure 10.** Typical AFM images of CoNiP films, (a) as-deposited and post-annealed under field of 0 T (b) and 9 T (c).

**Figure 10.** Typical AFM images of CoNiP films, (a) as-deposited and post-annealed under field of 0 T (b) and 9 T (c).

Grain size (nm) 32.2±3.4 97.53±5.5 44.6±2.6 Roughness (nm) 9.15±0.72 16.35±1.02 8.88±0.56

**(a)As deposited (b)B=0T (c)B=9T** 

**As deposited Annealed 0T Annealed 9T(**ⅲ**)**

(220)

**As deposited Annealed 0T Annealed 9T(**ⅲ**)**

(220)

 HCP-Co FCC-CoNiP FCC-Ni

As deposited

 HCP-Co FCC-CoNiP FCC-Ni

B=9T

B=9T

B=0T

B=0T

As deposited

**Table 5.** Grain size and roughness of the CoNiP films, before annealed and post-annealed under a 0 T or 9 T magnetic field.

Grain size (nm) 32.2±3.4 97.53±5.5 44.6±2.6 Roughness (nm) 9.15±0.72 16.35±1.02 8.88±0.56

magnified diffraction pattern between 42° and 48° of 2θ is shown in the inset of (A).

(100) (002)(A)

(111)

(111)

The XRD patterns of as deposited and post-annealed samples were shown in Figure 11. The

The XRD patterns of as deposited and post-annealed samples were shown in Figure 11. The magnified diffraction

The XRD patterns of as deposited and post-annealed samples were shown in Figure 11. The magnified diffraction

42 44 46 48

**Figure 11.** XRD patterns of as-deposited CoNiP film (a), and post-annealed under the magnetic field of : (b) B = 0 T; (c) B = 9 T. A magnified diffraction pattern between 42° and 48° is shown in the inset of (A).

The as-deposited CoNiP film showed a kind of fcc structure which was the *α*-phase of the Co-based alloy. After annealed at 673 K, an additional hcp-Co (002) peak around 45° appeared, since according to the research of Lew et al. [68] the <001> texture will form after annealed. In the case of annealed under field of 9 T, the (111) diffraction

We have studied the influence of high magnetic eld annealing on the grain growth and phase structure of pulse electrodeposition CoNiP films. FE-SEM and AFM studies showed that the grains size and the roughness were decreased after annealed under the high magnetic field. X-ray diffraction patterns showed that a mixed phase

**Note 1:** The main part, figures, and tables in **Section 3** have been published on Journal of Iron and Steel

magnetic field annealing on microstructure of pulse-electrodeposited nanocrystalline Co-Ni-P films. J

40 50 60 70 80 90

42 44 46 48

**Figure 11.** XRD patterns of as-deposited CoNiP film (a), and post-annealed under the magnetic field of : (b) B = 0 T; (c)

The as-deposited CoNiP film showed a kind of fcc structure which was the *α*-phase of the Cobased alloy. After annealed at 673 K, an additional hcp-Co (002) peak around 45° appeared, since according to the research of Lew et al. [68] the <001> texture will form after annealed. In the case of annealed under field of 9 T, the (111) diffraction peak of fcc-Ni and the (100) peak of hcp-Co were measured. This means a high magnetic field induces a mixed structure in the film that consists of fcc-Ni, hcp-Co together with fcc-CoNiP alloy. In addition, the diffraction peak (111) of *α*-phase shifts to lower diffraction angles in case of magnetic flux density of 9 T.

The as-deposited CoNiP film showed a kind of fcc structure which was the *α*-phase of the Co-based alloy. After annealed at 673 K, an additional hcp-Co (002) peak around 45° appeared, since according to the research of Lew et al. [68]the <001> texture will form after annealed. In the case of annealed under field of 9 T, the (111) diffraction peak of fcc-Ni and the (100) peak of hcp-Co were measured. This means a high magnetic field induces a mixed structure in the film that consists of fcc-Ni, hcp-Co together with fcc-CoNiP alloy. In addition, the diffraction peak (111) of *α*-phase shifts to lower diffraction angles in case of magnetic flux density of 9 T. This behavior can be rationalized as more Ni atoms are separated out of the CoNiP solid solution under a high magnetic field, resulting in a transition from Ni-like fcc-microstructural evolution to Co-like fcc-microstructural [69]. The XRD results reveal that during the electrodeposition process, the structure of supersaturated solid solution CoNiP (*α*-phase), is not stable. After annealing, Ni and Co atoms have a potential to separate out of the alloy, and an accelerating effect of

**Figure 11.** XRD patterns of as-deposited CoNiP film (a), and post-annealed under the magnetic field of : (b) B = 0 T; (c) B = 9 T. A magnified diffraction pattern between 42° and 48° is shown in the inset of (A).

(100) (002)(A)

(111)

(111)

40 50 60 70 80 90

2 (degrees)

2 (degrees)

**3.3.3 Crystal structure**

**3.4 Conclusion** 

*3.3.3. Crystal structure*

**3.3.3 Crystal structure**

278 Electroplating of Nanostructures

pattern between 42° and 48° of 2θ is shown in the inset of (A).

(002)

(111)

(200)

(111)

(100)

pattern between 42° and 48° of 2θ is shown in the inset of (A).

(002)

(111)

(200)

B = 9 T. A magnified diffraction pattern between 42° and 48° is shown in the inset of (A).

high magnetic field on diffusion modifies this tendency during the annealing process.

structure was formed in the annealed film under a 9 T magnetic field.

Research as: Li DG, Chun WU, Qiang W, Agnieszka F, He J-C. Influence of high

(111)

(100)

Intensity (a.u.)

Intensity (a.u.)

We have studied the influence of high magnetic field annealing on the grain growth and phase structure of pulse electrodeposition CoNiP films. FE-SEM and AFM studies showed that the grains size and the roughness were decreased after annealed under the high magnetic field. X-ray diffraction patterns showed that a mixed phase structure was formed in the annealed film under a 9 T magnetic field.

**Note 1:** The main part, figures, and tables in **Section 3** have been published on Journal of Iron and Steel Research as: Li DG, Chun WU, Qiang W, Agnieszka F, He J-C. Influence of high magnetic field annealing on microstructure of pulseelectrodeposited nanocrystalline Co-Ni-P films. J Iron Steel Res Int 2012;19:1085-8.

**Note 2:** The three sections in Chapter one is mainly about the influence of postannealing under high magnetic fields on the microsturcture of pulse-electrode‐ posited nanocrystalline Co-based films.

## **Author details**

Donggang Li1,3\*, Qiang Wang2\*, Agnieszka Franczak3 , Alexandra Levesque3 and Jean-Paul Chopart3

\*Address all correspondence to: lidonggang@smm.neu.edu.cn, wangq@mail.neu.edu.cn

1 School of Materials and Metallurgy, Northeastern University, Shenyang, China

2 Key Laboratory of Electromagnetic Processing of Materials (Ministry of Education), North‐ eastern University, Shenyang, China

3 LISM, Université de Reims Champagne-Ardenne, France

## **References**

[1] Baghbanan M, Erb U, Palumbo G. In: Mukhopadhyay SM, Seal S, Dahotre N, Agar‐ wal A, Smugeresky JE, Moody N. (eds.) Surface and Interfaces in Nanostructured Materials and Trends in LIGA, Miniaturization and Nanoscale Materials, The Miner‐ als, Metals and Materials Society, Warrendale, PA, 2004, pp. 307-315.


[15] Tang X, Dai J, Zhu X, Song W, Sun Y. Magnetic annealing effects on multiferroic Bi‐ FeO3/CoFe2O4 bilayered films, J Alloy Compd 2011;511:4748-53.

Materials and Trends in LIGA, Miniaturization and Nanoscale Materials, The Miner‐

[2] Cavallotti PL, Vicenzo A, Bestetti M, Franz S. Microelectrodeposition of cobalt and

[3] Tian L, Xu J, Qiang C. The electrodeposition behaviors and magnetic properties of

[4] Koza JA, Karnbach F, Uhlemann M, McCord J, Mickel C, Gebert A, Baunack S, Schultz L. Electrocrystallisation of CoFe alloys under the influence of external homo‐ geneous magnetic fields—Properties of deposited thin films, Electrochim Acta

[5] Georgescu V, Daub M. Magnetic field effects on surface morphology and magnetic properties of Co-Ni-P films prepared by electrodeposition, Surf Sci 2006;60:4195-9. [6] Krause A, Hamann C, Uhlemann M, Gebert A, Schultz L. Influence of a magnetic field on the morphology of electrodeposited cobalt, Magn Magn Mater

[7] Hibbard G, Erb U, Aus KT, Klement U, Palumbo G. Thermal stability of nanostruc‐

[8] Li YB, Lou YF, Zhang LR, Ma B, Bai JM, Wei FL. Effect of magnetic field annealing on microstructure and magnetic properties of FePt films, J Magn Magn Mater 2010 ;

[9] Markou A, Panagiotopoulos I, Bakas T. Effects of layering and magnetic annealing

[10] Li DS, Garmestani H, Yan S-S, Elkawni M, Bacaltchuk MB, Schneider-Muntau HJ, Liu JP, Saha S, Barnard JA. Effects of high magnetic field annealing on texture and

[11] Liu T, Li D, Wang Q, Wang K, Xu Z, He J. Enhancement of the Kirkendall effect in Cu-Ni diffusion couples induced by high magnetic fields, J Appl Phys

[12] Li D, Wang Q, Liu T, Li G, He J. Growth of diffusion layers at liquid Al-solid Cu in‐ terface under uniform and gradient high magnetic field conditions, Mater Chem

[13] Li D, Wang Q, Li G, Lv X, Nakajima K, He J. Diffusion layer growth at Zn/Cu inter‐ face under uniform and graident high magnetic fields, Mater Sci Eng A

[14] Coey JMD, Hinds G. Magnetic electrodeposition, J Alloy Compd 2001;326:238-45.

tured electrodeposits, Mater Sci Forum 2002;386-388:387-96.

on the texture of CoPt films, J Magn Magn Mater 2010 ;322:L61-3.

magnetic properties of FePd, J Magn Magn Mater 2004;281:272-5.

als, Metals and Materials Society, Warrendale, PA, 2004, pp. 307-315.

cobalt alloys for magnetic layers, Surf Coat Technol 2003;73:169-70.

Ni-Co films, Appl Surf Sci 2011;257:4689-94.

2010;55:819-31.

280 Electroplating of Nanostructures

2005;290-291:261-4.

322:3789-91.

2010;107:103542(1-3).

Phys 2009;117:504-10.

2008;495:244-8.


[44] Lee KH, Yoo J, Ko J, Kim H, Chung H, Chang D. Fabrication of biaxially textured Ni tape for YBCO coated conductor by electrodeposition, Phys C 2002;372:866-8.

[30] Wang L, Gao Y, Xue Q, Liu H, Xu T. Graded composition and structure in nanocrys‐ talline Ni-Co alloys for decreasing internal stress and improving tribological proper‐

[31] Armyanov S. Crystallographic structure and magnetic properties of electrodeposited

[32] Cavallotti PL, Vicenzo A, Bestetti M, Franz S. Microelectrodeposition of cobalt and

[33] Yu Y, Wei G, Hu X, Ge H, Yu Z. The effect of magnetic fields on the electroless depo‐

[34] Chopart J-P, Olivier A, Merienne E, Amblard J, Aaboubi O. New experimental device for convective mass-transport analysis by electrokinetic-hydrodynamic effect, Elec‐

[35] Levesque A, Chouchane S, Douglade J, Rehamnia R, Chopart J-P. Effect of natural and magnetic convections on the structure of electrodeposited zinc-nickel alloy, App

[36] Uhlemann M, Gebert A, Herrich M, Krause A, Cziraki A, Schultz L. Electrochemical deposition and modification of Cu/Co-Cu multilayer, Electrochim Acta

[37] Krause A, Uhlemann M, Gebert A, Schultz L. A study of nucleation, growth, texture and phase formation of electrodeposited cobalt layers and the influence of magnetic

[38] Krause A, Hamann C, Uhlemann M, Gebert A, Schultz L. Influence of a magnetic field on the morphology of electrodeposited cobalt, J Magn Magn Mat 2005;290:261-4.

[39] Franczak A, Levesque A, Bohr F, Douglade J, Chopart J-P. Structural and morpholog‐ ical modifications of the Co-thin films caused by magnetic field and pH variation,

[40] Li D, Levesque A, Franczak A, Wang Q, He J, Chopart J-P. Evolution of morphology in electrodeposited nanocrystalline Co-Ni films by in-situ high magnetic field appli‐

[41] Koza JA, Uhlemann M, Gebert A, Schultz L. Nucleation and growth of the electrode‐ posited iron layers in the presence of an external magnetic field, Electrochim Acta

[42] Li X, Ren Z, Fautrelle Y. Alignment behavior of the primary Al3Ni phase in Al-Ni

[43] Krause A, Uhlemann M, Gebert A, Schultz L. The effect of magnetic fields on the

alloy under a high magnetic field, J Crystal Grwth 2008;310:3488-97.

electrodeposition of cobalt, Electrochim Acta 2004;49:4127-34.

ties, J Phys D: App Phys 2005;38:1318-24.

trochem Sol Sta Lett 1998;1:139-41.

fields, Thin Solid Films 2006;515:1694-700.

App Surf Sci 2012;258:8683-8.

cation, Talanta 2013;110(15):66-70.

Surf Sci 2009;255:8048-53.

2003;48:3005-11.

282 Electroplating of Nanostructures

2008;53:7972-80.

cobalt and cobalt alloys, Electrochim Acta 2000;45:3323-35.

sition of Co-W-P film, Surf Coat Tech 2010;204:2669-76.

cobalt alloys for magnetic layers, Surf Coat Technol 2003;169:76-80.

