# Electronic Controlling on Nanotribological Properties of a Textured Surface by Laser Processing

Authors: Haifeng Yang; Kun Liu; Yanqing Wang; Hao Liu; Jiaxiang Man; Bo Sun
Journal: Journal of Spectroscopy
 (2017)

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## Abstract

The friction-reducing performance of surfaces with regular nanotextures is a key topic in surface engineering research. This paper presented a simple, easily controlled method for fabricating regular nanotextures on an electrodeposited Ni-Co alloy. The electronic controlling on the friction performance of a nanotexured surface was investigated by AFM. The results showed that the frictional force of a nanotexured surface can be controlled by an external electric field. Before laser processing, the friction initially increased with the bias voltage and then decreased after the bias voltage exceeded 1.0 V. Its friction forces can be changed more than 2 times under the different external electric field. After laser processing, the trend of the frictional force was reversed and its friction forces changed more than 12 times for the laser-processed sample with 0.18 J/cm2 laser power. The results also showed that the friction force decreased when using different nanotextures in an external electric field.


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## Body

## 1. Introduction

In computing and MEMS areas, Ni-Co coating was widely applied in such devices as microforceps, micromirrors, and microswitches. Usually, these devices worked under an external electric field. However, the effect of this external electric field on the friction performance of Ni-Co coatings was rarely studied. Meanwhile, it can also be used in the controlling of the friction coefficient or maintaining its stability.Through controlling the surface characteristics, an engineered surface can be made to deliver the desired functional performance [1]. Except for a wide range of other applications of laser technique [2–4], as an effective technique, it also was used to improving the coating performances [5–8]. Many researchers have investigated the laser processing technique about how to improve surface performance of alloy coatings [9–11]. Nowadays, methods such as moulding [12], electrochemical deposition [13, 14], and chemical vapor deposition [15] are used to produce artificial surfaces with particular textures. However, all of these methods fail to produce controllable textured surfaces. In recent years, many researchers have adopted new processes to fabricate textures on solid surfaces. Mo et al. fabricated the nanotexture on an H-passivated Si surface by current-induced local anodic oxidation and investigated its nanotribological properties by colloidal probe [16, 17]. The results indicated that the nanotextures exhibited low adhesion and greatly reduced the friction at a nanometric scale. Fang Liang investigated the friction and wear of a 45# steel surface textured by YAG laser and found that the coefficient of friction of a cross-grooved surface increased with decreasing texture span (i.e., width of pattern). The tribological properties of nanotextures on Ni-Co coatings have not been extensively studied to date.In recent years, many researchers have investigated the relationship between the nanotribological properties and external electric field at nanoscale in different domains. Park et al. found that the nanoscale friction properties of a Si (100) sample can be manipulated significantly by the simple application of a bias voltage [18]. They then observed a significant increase in friction under accumulation (forward bias) conditions with respect to depletion (reverse bias) conditions and established a model based on the force exerted by the trapped charges that quantified the experimental observations of excess friction, using a Pt-coated tip with a 50 nm radius in an AFM sliding against an n-type GaAs (100) substrate [19]. Liu et al. investigated the microtribological properties of Langmuir-Blodgett monolayer films in AC and DC electric fields [20]. They found that the friction and wear characteristics of Langmuir-Blodgett films could be controlled and improved by an external electric field. However, the influence of an external electric field on the friction properties of nanotexures on a Ni-Co coating has not previously been studied.Here, the nanotextures on the Ni-Co alloy coating surface were fabricated by the laser processing technique. The surface morphology and microstructure of the laser-processed region were characterized by SEM. Then, the nanotribological behavior of different nanotexured surfaces under external electrical field was investigated by FFM and AFM.


## 2. Experiments

### 2.1. Experimental Setup

The experimental setup for the electroplating is shown in Figure1(a). A type of CHI660D electrochemical workstation was used to provide power supply. Figure 1(b) showed the laser processing experimental system for fabricating nanotextures on the electroplated Ni-Co alloy coating surface. An ultraviolet laser (DSH-355-10, Photonics Industries, USA) with a working wavelength of 355 nm was used to process the specimen. The laser beam was completely reflected by two mirrors. The reflected beam was filled, collimated, and expanded by a beam expander. The beam expander could allow the high-frequency noise to be removed from the laser beam to provide a clean Gaussian profile and make the laser beam smaller after focusing. A computer-controlled laser marker was used to control the direction of the laser beam.Figure 1
(a) Schematic of the electroplating setup. (b) Laser processing experimental system.
(a)
(b)


### 2.2. Experimental Method

Before the electroplating of Ni-Co alloy coating, the bath composition was prepared according to Table1. To ensure that the composition of the bath was uniform, the electrolyte was subject to magnetic stirring for 20 min before the deposition process started. A nickel sample, of commercial-purity grade, measuring 80 mm × 60 mm × 2 mm was used as the anode, and a type 316L stainless steel specimen, measuring 20 mm × 10 mm × 2 mm, was used as the cathode. The cathode was placed 30 mm from, and parallel to, the nickel when immersed in the bath. Before electroplating, the specimen was polished using 2000 grit and then degreased in acetone under ultrasonic vibration for 5 min and then pretreated in 1 mol/L HCL solution for 2 min at room temperature to remove the surface oxide scale.Table 1
The composition of the electroplating bath solution and relevant processing parameters.
Composition
Content/gL−1
Cobalt sulphate
30
Nickel sulphate
250
Nickel chloride
40
Boric acid
35
Code position condition
Temperature (°C)
50
pH
3.5 to 4.5Then, the electroplating was performed under direct current conditions with the current density of 25 mA/cm2 and electroplating time of 20 min. After electroplating, distilled water was used to wash the specimen. The specimen was tested after being dried at room temperature in air for several hours. The deposition thickness was about 8 μm. The surface morphology and microstructure of the coating were characterized by SEM.After that, the laser processing experimental system was used to fabricate nanotextures on the electroplated Ni-Co alloy coating. The laser power ranged from 0 J/cm2 to 2 J/cm2 at a scan speed of 25.4 mm/s and line interval of 0.01 mm. The SEM was used to analyze the effect of laser irradiation on the surface morphology and microstructure of the coating.Lastly, the nanotribological behavior of the Ni-Co alloy coating in this electric field was measured by AFM/FFM (CSPM5500 electronics, Benyuan Nano-Instruments, China). The probe was coated with a conducting layer of Au film. The varying load (0.1 to 1.0 V) and bias voltage (0.0 V, 0.5 V, 1.0 V, 1.5 V, and 2.0 V) were applied between the probe and the sample.


## 2.1. Experimental Setup

The experimental setup for the electroplating is shown in Figure1(a). A type of CHI660D electrochemical workstation was used to provide power supply. Figure 1(b) showed the laser processing experimental system for fabricating nanotextures on the electroplated Ni-Co alloy coating surface. An ultraviolet laser (DSH-355-10, Photonics Industries, USA) with a working wavelength of 355 nm was used to process the specimen. The laser beam was completely reflected by two mirrors. The reflected beam was filled, collimated, and expanded by a beam expander. The beam expander could allow the high-frequency noise to be removed from the laser beam to provide a clean Gaussian profile and make the laser beam smaller after focusing. A computer-controlled laser marker was used to control the direction of the laser beam.Figure 1
(a) Schematic of the electroplating setup. (b) Laser processing experimental system.
(a)
(b)


## 2.2. Experimental Method

Before the electroplating of Ni-Co alloy coating, the bath composition was prepared according to Table1. To ensure that the composition of the bath was uniform, the electrolyte was subject to magnetic stirring for 20 min before the deposition process started. A nickel sample, of commercial-purity grade, measuring 80 mm × 60 mm × 2 mm was used as the anode, and a type 316L stainless steel specimen, measuring 20 mm × 10 mm × 2 mm, was used as the cathode. The cathode was placed 30 mm from, and parallel to, the nickel when immersed in the bath. Before electroplating, the specimen was polished using 2000 grit and then degreased in acetone under ultrasonic vibration for 5 min and then pretreated in 1 mol/L HCL solution for 2 min at room temperature to remove the surface oxide scale.Table 1
The composition of the electroplating bath solution and relevant processing parameters.
Composition
Content/gL−1
Cobalt sulphate
30
Nickel sulphate
250
Nickel chloride
40
Boric acid
35
Code position condition
Temperature (°C)
50
pH
3.5 to 4.5Then, the electroplating was performed under direct current conditions with the current density of 25 mA/cm2 and electroplating time of 20 min. After electroplating, distilled water was used to wash the specimen. The specimen was tested after being dried at room temperature in air for several hours. The deposition thickness was about 8 μm. The surface morphology and microstructure of the coating were characterized by SEM.After that, the laser processing experimental system was used to fabricate nanotextures on the electroplated Ni-Co alloy coating. The laser power ranged from 0 J/cm2 to 2 J/cm2 at a scan speed of 25.4 mm/s and line interval of 0.01 mm. The SEM was used to analyze the effect of laser irradiation on the surface morphology and microstructure of the coating.Lastly, the nanotribological behavior of the Ni-Co alloy coating in this electric field was measured by AFM/FFM (CSPM5500 electronics, Benyuan Nano-Instruments, China). The probe was coated with a conducting layer of Au film. The varying load (0.1 to 1.0 V) and bias voltage (0.0 V, 0.5 V, 1.0 V, 1.5 V, and 2.0 V) were applied between the probe and the sample.


## 3. Results and Discussions

### 3.1. Laser-Induced Nanotextures on the Ni-Co Alloy Coating

The laser power was varied to investigate the influence on the Ni-Co alloy coating. The laser power was increased from 0 J/cm2 to 0.22 J/cm2. Figure 2 shows the micrographs of the Ni-Co alloy surfaces after laser processing at 0 J/cm2, 0.03 J/cm2, 0.05 J/cm2, 0.08 J/cm2, 0.18 J/cm2, and 0.22 J/cm2.Figure 2
SEM images of Ni-Co alloy coating surface. (a) Unprocessed; laser processed at (b) 0.03 J/cm2; (c) 0.05 J/cm2; (d) 0.08 J/cm2; (e) 0.18 J/cm2; (f) 0.22 J/cm2.
(a)
(b)
(c)
(d)
(e)
(f)The morphology of the Ni-Co alloy coating before laser process was shown in Figure2(a). Many irregular-sized microparticles and nanoprotrusions were observed. The average diameter of the grains was approximately 0.7 μm. The Co content in the coating accounted for 40% of its total mass. The roughness Ra of the Ni-Co coating surface was approximately 25 nm. After laser processing at 0.03 J/cm2, most of the irregular protrusions become half-hemispherical and more regular and the surface morphology of the laser-processed area was also uneven (Figure 2(b)). With increase of laser power, the half-hemispherical nanoprotrusions grew uniformly and gradually became half-ellipsoid structures. Besides, when the laser powers were 0.05 and 0.08 J/cm2, the surface morphology of the laser-processed area becomes flatter, as shown in Figures 2(c) and 2(d). At 0.18 J/cm2, the half-hemispherical nanoprotrusions continued to grow and began to reduce in number (Figure 2(e)). Figure 2(f) showed that the surface morphology of the laser-processed area had become relatively smooth at 0.22 J/cm2 and the nanoprotrusions had completely disappeared.Through these experiments, we concluded that the formation of regular nanoprotrusions was dependent on the power of the ultraviolet laser. Therefore, we can adjust the power of the ultraviolet laser for fabricating stable nanoprotrusions on the surface of the Ni-Co alloy coating. Koch et al. and Mannion et al. once proposed a theory in which nanoprotrusions were formed because of the interference between the incident laser and the excited surface electromagnetic waves caused by the presence of structural defects [21, 22]. This theory can be also used to explain the formation of nanoprotrusions on the surface of the Ni-Co alloy coating. Moreover, after laser irradiation, vaporization and redeposition of the nanoparticles should also affect the surface nanostructures. However, the detailed mechanism underpinning this behavior requires further investigation [23]. When the applied laser power was greater than 0.22 J/cm2, the Ni-Co alloy coating underwent rapid fusion due to extreme heat. Therefore, the surface morphology of the laser-processed area became smooth, and the nanoprotrusions on the surface almost all vanished.


### 3.2. Nanotribological Properties under Different Bias Voltages

Figure3 showed the different relationships between the frictional force and normal load at bias voltages of 0 V, 0.5 V, 1.0 V, 1.5 V, and 2.0 V. It can be seen that the friction increased quasilinearly with increasing normal load for the different Ni-Co alloy coating surfaces.Figure 3
Frictional force versus normal load, from 0.1 V to 1.0 V, with five bias voltages (0 V, 0.5 V, 1 V, 1.5 V, and 2 V) for the four Ni-Co alloy coating surfaces. (a) unprocessed; laser processed at (b) 0.03 J/cm2; (c) 0.05 J/cm2; (d) 0.18 J/cm2.
(a)
(b)
(c)
(d)In Figure3(a), for unprocessed specimen, the friction force with a forward bias voltage was larger than that without a bias voltage. Its friction forces can be changed more than 2 times under the different external electric field. However, the situation was reversed in Figures 3(b), 3(c), and 3(d). This difference in the frictional forces was mainly due to changes in the surface crystal lattice and texture that can influence the friction between metal friction pairs [24]. It may be concluded that the bias voltage can be increased to reduce friction on the surface after laser processing. In particular, the friction force under a bias voltage was significantly reduced (Figure 3(d)). Its friction forces changed more than 12 times for this specimen. Therefore, the nanotribological properties were affected by laser irradiation under a forward bias voltage.Figure4 showed the relationship between frictional force and the bias voltages of 0.0 V, 0.5 V, 1.0 V, 1.5 V, and 2.0 V with four normal loads (0.19 V, 0.39 V, 0.59 V, and 0.79 V). The frictional force could be controlled by external electric field. In Figure 4(a), the frictional force initially increased with increasing bias voltage but then decreased while the bias voltage exceeded 1.0 V at normal loads of 0.19 V, 0.39 V, 0.59 V, and 0.79 V. However, the frictional force initially decreased with increasing bias voltage and then increased as shown in Figures 4(b), 4(c), and 4(d). The trend varied, mainly due to the changes in the surface crystal lattice and texture [25].Figure 4
Frictional force versus bias voltage, from 0 V to 2 V, at four normal loads (0.19 V, 0.39 V, 0.59 V, and 0.79 V) for the four Ni-Co alloy coating surfaces. (a) Unprocessed; laser processed at (b) 0.03 J/cm2; (c) 0.05 J/cm2; (d) 0.18 J/cm2.
(a)
(b)
(c)
(d)There are two main theories which may be used to interpret these behaviors: electrostatic interaction theory and self-generated voltage theory. Electrostatic interaction theory dictated that the external electric field can influence the electrostatic force between friction pairs and thus affects the real normal load (Preal). The sphere-plane electrostatic adhesion force (Fe) is related to the voltage of the external electronic field (U). When the bias voltage exceeds 0 V, the real normal load initially decreases with increasing bias voltage and then it increased, which matched the measured results. Self-generated voltage theory said that during the repeated relative movement of the tip and sample surface, the friction between metal friction pairs would self-generate a voltage Vg [24–26], the direction of which might be contrary to the external electric voltage Ve. Thereinto, the self-generated voltage Vg increases as the number of repeating relative movements between the tip and sample surface increases [25]. Thus, the actual bias voltage Va between tip and sample surface is Va=Ve−Vg. After laser treatment, the changes in the surface crystal lattice and texture affected the rate of increase of Vg. This trend is reversed after laser irradiation, because of the differing rates of increase of Vg and Ve.


### 3.3. Nanotribological Properties of Different Nanotextures

Figure5 showed the variation in friction force and normal load for different sample surfaces (unprocessed and processed at 0.03 J/cm2, 0.05 J/cm2, and 0.18 J/cm2). Figure 5(a) showed a plot of the frictional force versus normal load at the same bias voltage Ve of 0 V. According to the comparison of the sample before and after laser processing, the differences between the trends were not clear. A plot of the frictional force versus normal load at the same bias voltages Ve of 0.5 V, 1.0 V, and 2.0 V were shown separately in Figures 5(b), 5(c), and 5(d). When the bias voltage exceeded 0 V, the differences between the changing trends of the surface friction force become distinct: after laser processing, the surface friction was significantly lower than before. Thus, the frictional force can be controlled through the use of laser processing under a forward bias voltage. In Figure 5, as the surface became smooth after laser processing at 0.18 J/cm2, the frictional force changed between approximately between 0.05 V and 0.1 V under a bias voltage of 0 V and varied between 0 V and 0.05 V when the bias voltage exceeded 0 V. To some extent, the frictional force remained stable. Therefore, under an external electrical field and specific laser processing, the Ni-Co alloy surface frictional force can be controlled so as to be reduced by the nanotexture deposited on the Ni-Co alloy coating.Figure 5
Frictional force versus normal load for the different sample surfaces under four constant bias voltages. (a) 0 V; (b) 0.5 V; (c) 1.0 V; (d) 2.0 V.
(a)
(b)
(c)
(d)


## 3.1. Laser-Induced Nanotextures on the Ni-Co Alloy Coating

The laser power was varied to investigate the influence on the Ni-Co alloy coating. The laser power was increased from 0 J/cm2 to 0.22 J/cm2. Figure 2 shows the micrographs of the Ni-Co alloy surfaces after laser processing at 0 J/cm2, 0.03 J/cm2, 0.05 J/cm2, 0.08 J/cm2, 0.18 J/cm2, and 0.22 J/cm2.Figure 2
SEM images of Ni-Co alloy coating surface. (a) Unprocessed; laser processed at (b) 0.03 J/cm2; (c) 0.05 J/cm2; (d) 0.08 J/cm2; (e) 0.18 J/cm2; (f) 0.22 J/cm2.
(a)
(b)
(c)
(d)
(e)
(f)The morphology of the Ni-Co alloy coating before laser process was shown in Figure2(a). Many irregular-sized microparticles and nanoprotrusions were observed. The average diameter of the grains was approximately 0.7 μm. The Co content in the coating accounted for 40% of its total mass. The roughness Ra of the Ni-Co coating surface was approximately 25 nm. After laser processing at 0.03 J/cm2, most of the irregular protrusions become half-hemispherical and more regular and the surface morphology of the laser-processed area was also uneven (Figure 2(b)). With increase of laser power, the half-hemispherical nanoprotrusions grew uniformly and gradually became half-ellipsoid structures. Besides, when the laser powers were 0.05 and 0.08 J/cm2, the surface morphology of the laser-processed area becomes flatter, as shown in Figures 2(c) and 2(d). At 0.18 J/cm2, the half-hemispherical nanoprotrusions continued to grow and began to reduce in number (Figure 2(e)). Figure 2(f) showed that the surface morphology of the laser-processed area had become relatively smooth at 0.22 J/cm2 and the nanoprotrusions had completely disappeared.Through these experiments, we concluded that the formation of regular nanoprotrusions was dependent on the power of the ultraviolet laser. Therefore, we can adjust the power of the ultraviolet laser for fabricating stable nanoprotrusions on the surface of the Ni-Co alloy coating. Koch et al. and Mannion et al. once proposed a theory in which nanoprotrusions were formed because of the interference between the incident laser and the excited surface electromagnetic waves caused by the presence of structural defects [21, 22]. This theory can be also used to explain the formation of nanoprotrusions on the surface of the Ni-Co alloy coating. Moreover, after laser irradiation, vaporization and redeposition of the nanoparticles should also affect the surface nanostructures. However, the detailed mechanism underpinning this behavior requires further investigation [23]. When the applied laser power was greater than 0.22 J/cm2, the Ni-Co alloy coating underwent rapid fusion due to extreme heat. Therefore, the surface morphology of the laser-processed area became smooth, and the nanoprotrusions on the surface almost all vanished.


## 3.2. Nanotribological Properties under Different Bias Voltages

Figure3 showed the different relationships between the frictional force and normal load at bias voltages of 0 V, 0.5 V, 1.0 V, 1.5 V, and 2.0 V. It can be seen that the friction increased quasilinearly with increasing normal load for the different Ni-Co alloy coating surfaces.Figure 3
Frictional force versus normal load, from 0.1 V to 1.0 V, with five bias voltages (0 V, 0.5 V, 1 V, 1.5 V, and 2 V) for the four Ni-Co alloy coating surfaces. (a) unprocessed; laser processed at (b) 0.03 J/cm2; (c) 0.05 J/cm2; (d) 0.18 J/cm2.
(a)
(b)
(c)
(d)In Figure3(a), for unprocessed specimen, the friction force with a forward bias voltage was larger than that without a bias voltage. Its friction forces can be changed more than 2 times under the different external electric field. However, the situation was reversed in Figures 3(b), 3(c), and 3(d). This difference in the frictional forces was mainly due to changes in the surface crystal lattice and texture that can influence the friction between metal friction pairs [24]. It may be concluded that the bias voltage can be increased to reduce friction on the surface after laser processing. In particular, the friction force under a bias voltage was significantly reduced (Figure 3(d)). Its friction forces changed more than 12 times for this specimen. Therefore, the nanotribological properties were affected by laser irradiation under a forward bias voltage.Figure4 showed the relationship between frictional force and the bias voltages of 0.0 V, 0.5 V, 1.0 V, 1.5 V, and 2.0 V with four normal loads (0.19 V, 0.39 V, 0.59 V, and 0.79 V). The frictional force could be controlled by external electric field. In Figure 4(a), the frictional force initially increased with increasing bias voltage but then decreased while the bias voltage exceeded 1.0 V at normal loads of 0.19 V, 0.39 V, 0.59 V, and 0.79 V. However, the frictional force initially decreased with increasing bias voltage and then increased as shown in Figures 4(b), 4(c), and 4(d). The trend varied, mainly due to the changes in the surface crystal lattice and texture [25].Figure 4
Frictional force versus bias voltage, from 0 V to 2 V, at four normal loads (0.19 V, 0.39 V, 0.59 V, and 0.79 V) for the four Ni-Co alloy coating surfaces. (a) Unprocessed; laser processed at (b) 0.03 J/cm2; (c) 0.05 J/cm2; (d) 0.18 J/cm2.
(a)
(b)
(c)
(d)There are two main theories which may be used to interpret these behaviors: electrostatic interaction theory and self-generated voltage theory. Electrostatic interaction theory dictated that the external electric field can influence the electrostatic force between friction pairs and thus affects the real normal load (Preal). The sphere-plane electrostatic adhesion force (Fe) is related to the voltage of the external electronic field (U). When the bias voltage exceeds 0 V, the real normal load initially decreases with increasing bias voltage and then it increased, which matched the measured results. Self-generated voltage theory said that during the repeated relative movement of the tip and sample surface, the friction between metal friction pairs would self-generate a voltage Vg [24–26], the direction of which might be contrary to the external electric voltage Ve. Thereinto, the self-generated voltage Vg increases as the number of repeating relative movements between the tip and sample surface increases [25]. Thus, the actual bias voltage Va between tip and sample surface is Va=Ve−Vg. After laser treatment, the changes in the surface crystal lattice and texture affected the rate of increase of Vg. This trend is reversed after laser irradiation, because of the differing rates of increase of Vg and Ve.


## 3.3. Nanotribological Properties of Different Nanotextures

Figure5 showed the variation in friction force and normal load for different sample surfaces (unprocessed and processed at 0.03 J/cm2, 0.05 J/cm2, and 0.18 J/cm2). Figure 5(a) showed a plot of the frictional force versus normal load at the same bias voltage Ve of 0 V. According to the comparison of the sample before and after laser processing, the differences between the trends were not clear. A plot of the frictional force versus normal load at the same bias voltages Ve of 0.5 V, 1.0 V, and 2.0 V were shown separately in Figures 5(b), 5(c), and 5(d). When the bias voltage exceeded 0 V, the differences between the changing trends of the surface friction force become distinct: after laser processing, the surface friction was significantly lower than before. Thus, the frictional force can be controlled through the use of laser processing under a forward bias voltage. In Figure 5, as the surface became smooth after laser processing at 0.18 J/cm2, the frictional force changed between approximately between 0.05 V and 0.1 V under a bias voltage of 0 V and varied between 0 V and 0.05 V when the bias voltage exceeded 0 V. To some extent, the frictional force remained stable. Therefore, under an external electrical field and specific laser processing, the Ni-Co alloy surface frictional force can be controlled so as to be reduced by the nanotexture deposited on the Ni-Co alloy coating.Figure 5
Frictional force versus normal load for the different sample surfaces under four constant bias voltages. (a) 0 V; (b) 0.5 V; (c) 1.0 V; (d) 2.0 V.
(a)
(b)
(c)
(d)


## 4. Conclusions

This paper presented a simple, easily controlled laser processing method for fabricating regular nanotextures on the electrodeposited Ni-Co alloy surface. The electronic controlling on the friction performance of the nanotexured surface was achieved using atomic force microscope. Regular nanoprotrusions can be produced by choosing certain laser processing parameters, and the frictional force on such nanotexured surfaces can be controlled by an external electric field. Before laser processing, the friction initially increased with the bias voltage and then decreased after the bias voltage exceeded 1.0 V. Its friction forces can be changed more than 2 times under the different external electric field. After laser processing, the trend of the frictional force was reversed and its friction forces changed more than 12 times for the laser-processed sample with 0.18 J/cm2 laser power. Furthermore, with certain nanotextures and bias voltages, the frictional force could be maintained at a stable value.



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*Source: 7920652-2017-09-06.xml*