Rippled polymer surface generated by stick-slip friction - Langmuir

Subscriber access provided by EKU Libraries

New Concepts at the Interface: Novel Viewpoints and Interpretations, Theory and Computations

Rippled polymer surface generated by stick-slip friction Conglin Dong, Chengqing Yuan, Aijie Xu, Xiuqin Bai, and Yu Tian Langmuir, Just Accepted Manuscript • DOI: 10.1021/acs.langmuir.8b04068 • Publication Date (Web): 28 Jan 2019 Downloaded from http://pubs.acs.org on January 30, 2019

Just Accepted “Just Accepted” manuscripts have been peer-reviewed and accepted for publication. They are posted online prior to technical editing, formatting for publication and author proofing. The American Chemical Society provides “Just Accepted” as a service to the research community to expedite the dissemination of scientific material as soon as possible after acceptance. “Just Accepted” manuscripts appear in full in PDF format accompanied by an HTML abstract. “Just Accepted” manuscripts have been fully peer reviewed, but should not be considered the official version of record. They are citable by the Digital Object Identifier (DOI®). “Just Accepted” is an optional service offered to authors. Therefore, the “Just Accepted” Web site may not include all articles that will be published in the journal. After a manuscript is technically edited and formatted, it will be removed from the “Just Accepted” Web site and published as an ASAP article. Note that technical editing may introduce minor changes to the manuscript text and/or graphics which could affect content, and all legal disclaimers and ethical guidelines that apply to the journal pertain. ACS cannot be held responsible for errors or consequences arising from the use of information contained in these “Just Accepted” manuscripts.

is published by the American Chemical Society. 1155 Sixteenth Street N.W., Washington, DC 20036 Published by American Chemical Society. Copyright © American Chemical Society. However, no copyright claim is made to original U.S. Government works, or works produced by employees of any Commonwealth realm Crown government in the course of their duties.

Page 1 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

Rippled polymer surface generated by stick–slip friction Conglin Donga,b,c, Chengqing Yuanb,c, Aijie Xua, Xiuqin Baib,c, Yu Tiana* a

b

State Key Laboratory of Tribology, Tsinghua University, Beijing 100084, China

Key Laboratory of Marine Power Engineering & Technology (Ministry of Transport), Wuhan University of Technology, Wuhan 430063, P.R. China

c

Reliability Engineering Institute, National Engineering Research Center for Water Transport Safety, Wuhan University of Technology, Wuhan 430063, P.R. China

Abstract: Textured surfaces with varied functionalities are generally fabricated by etching, cutting, or printing. In this study, different from the usual generation of grooves along the sliding direction in friction, regular parallel ripples that are perpendicular to the sliding direction were generated on a polymer surface by the stick–slip friction of polymer/metal friction pairs lubricated with water. Ripple height was proportional to the peak friction force in the sticking process. Ripple wave length decreased as the sliding velocity increased. The generation of ripples were ascribed to the adhesion and plastic deformation during stick–slip motion. The achieved rippled surface effectively improved the lubrication property of the two surfaces. These findings demonstrate a new method of in situ manufacturing ripples on a soft material surface through a controlled traditional sliding friction and also provide a new insight into the stick–slip friction behavior of materials.

Keywords: sliding friction, polymer, perpendicular ripples, stick–slip phenomenon.

*Corresponding

author: Yu TIAN.

E-mail address: [email protected].

ACS Paragon Plus Environment 1

Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60



Page 2 of 17

INTRODUCTION In nature and industries, many physical processes involved in energy exchange, motion, and signal

transmission are realized through surfaces, such as superhydrophobic surfaces, drag reduction surfaces, and optical components.[1–4] Given the comprehensive understanding of the physical and chemical phenomena of microscopic surfaces, the design and manufacture of surface switch microscopic structures are widely applied in anti-adhesion, vibration reduction, anti-friction and wear, electricity system, and other fields.[5–8] Many advanced manufacturing technologies, including laser processing, photolithography, electrolytic processing, honing, nanoindentation, reactive ion etching, abrasive blasting, embossing, and pulsed air arc, have been developed.[9–14] Thus, solid surfaces can now have micro pits, grooves, lug bosses and special microstructures with different shapes, sizes, and distributions to improve their material, physical, and chemical properties.[15,16] However, soft materials, such as rubber, plastic materials, and colloidal materials, are difficult to get regular microsurface textures on their surface using conventional mechanical cutting or molding processes.[17–19] In a general sliding friction process, grooves are usually generated along the sliding direction due to the scratches on surfaces caused by rough peaks or wear particles.[20,21] Stick–slip is a key friction phenomenon that is closely related to the friction mechanism and various industrial applications.[22–25] Classical theories suggest that stick–slip friction involves periodic adhesive contact during the sticking process and shear separation during the slipping process and produces surface wear and deformation.[26–28] With good elastic resilience, the deformation of rubbers can almost fully recover to the original morphology after being subjected to shearing.[29,30] However, the deformation of plastic materials cannot completely recover.[31–34] Residual plastic deformations might form a textured structure on the wear surface and further reflect stick–slip behavior.[35–37] The temperature of a polymer surface usually increases sharply under dry friction because of the poor thermal conductivity of polymer surface, and the polymer becomes soft and adhere to the counterpart and destroyed surfaces.[18] Schallamach observed that when a rigid sphere slides on a polymer surface, folds are generated at the contact zone of the polymer surface due to the rigid sphere squeezing the polymer surface, thereby causing plastic deformations. The analogy was used for the progression of a carpet ruck over a ﬂoor, which results in the movement of the carpet without requiring any sliding at the ﬂoor–carpet interface.[38,39] However, the ball could generate a deep and wide groove on the wear surface. In this study, a commercially available polyethylene was used as the test specimen. We observed the generation of regular ripples perpendicular to the sliding direction in polymer/metal friction lubricated with water. The relationship between ripple generation and friction behavior was systematically investigated and developed into a novel method for surface patterning. This work improves our understanding of stick–slip behavior between


Page 3 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

two surfaces.



MATERIALS AND METHODS

Experimental Materials. As a typical plastic material, polyethylene was used as square pin specimens in this study. Its infrared spectroscopy, thermogravimetric analysis, and basic physical properties at room temperature are shown in Figure 1. The length, width, and height of the specimens were 8, 8, and 20 mm, respectively, as shown in Figure 2(a). The plastic surfaces were polished before testing to a mean surface roughness (Sa) of approximately 0.02 ± 0.01 µm (white light interferometer, Micro Xam, ADEP Hase Shift, Inc., Tucson, AZ, USA). The counterpart of the polymer was a 1Cr18Ni9Ti stainless steel plate with a diameter of 80 mm and a thickness of 10 mm. Its surface roughness (Sa) was 0.02 ± 0.01 µm measured using the same white light interferometer mentioned above.

Figure 1. (a) Infrared spectroscopy, (b) thermogravimetric analysis, and (c) basic physical properties of polyethylene at room temperature.

Experimental Apparatus and Sliding Wear Tests. All friction tests were conducted on a commercial pin-on-disc friction testing machine (UMT-3 tribo-tester, Center for Tribology, Inc.). The applied nominal pressures were set to 0.5, 1.0, 1.5, 2, 2.5, and 3 MPa. The radius of the sliding track was 30 mm. The rotational speeds were set to 1, 3, 6, 9, 12, 15, and 18 r/min, which corresponded to sliding velocities of 3.14, 9.42, 18.84, 28.26, 37.68, 47.1, and 56.52 mm/s, respectively. The duration of each test was 3 min. Different test times of 10, 30, 60, 90, 120, 150, and 180 s were applied. To investigate the effects of ripple on coefficient of friction (COF), test polymer pins with ripples


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 4 of 17

were obtained under water lubrication at 3 MPa and 9.42 mm/s. Sliding velocities of 3.14, 9.42, 18.84, 28.26, 37.68, 47.1, 56.52, 94.2, 188.4, and 376.8 mm/s were applied under oil-lubricated conditions. The applied nominal pressures were 0.1, 0.2, 0.3, 0.4, 0.5, and 1 MPa. All tests were replicated several times to check the repeatability of the experiments. Friction force was measured every 0.01 s during the tests. A new plastic pin and a new 1Cr18Ni9Ti plate were used for each test.

Measurement Techniques and Procedures. The surface topographies of the tested polymer pins were examined with

a

JSM-6701F

scanning

electron

microscope

(JEOL,

Japan)

and an atomic

force

microscope

(MFP-3D Classic, Asylum Research, Santa Barbara, CA, USA). The infrared spectroscopy of polyethylene was determined using a Fourier transform infrared spectrometer (Thermo Scientific Nicolet iS5, America). A thermal gravimetric analyzer (THERMOSTEP, Eltra, Germany) was used to perform thermogravimetric analysis and initial temperature of thermal decomposition for polyethylene. The static and dynamic contact angles were characterized using a contact angle measuring instrument (DSA 100, KRUSS GmbH, Germany) at 20 °C. The mechanical properties of polyethylene, including elongation at break, tensile strength, and tear strength, were measured using a mechanical testing instrument (Instron 5967, INSTRON, China). The shore hardness of the composite was measured with a shore durometer (ASKER-A, ASKER, Japan). The yield strength, elastic model, and Poisson’s ratio of the material were examined using an electronic universal material testing machine (5967B12494, Instron LTD., America).



RESULTS AND DISCUSSION

Generating ripples. Friction tests were conducted on a commercial pin-on-disc tribo-tester (UMT-3 tribo-tester, Center for Tribology, Inc.), as shown in Figure 2(a). The upper polymer pin specimen was kept stationary, whereas the lower 1Cr18Ni9Ti plate specimen was rotated against the upper pin specimen under water lubrication. Figure 2(b) presents the typical stick–slip force under two loads of 1 and 3 MPa. The friction force under high load was much larger than that at low load, and a large decrease in friction force was observed during the slipping process. Parallel and regular ripples perpendicular to the sliding direction on the upper polymer surface were observed, as shown in Figure 2(c). As shown in Figures 2(d) and 2(e), the height of the ripples under high load was larger than that under low load. The friction force and perpendicular ripple indicated that a high load induced an obvious stick–slip phenomenon.


Page 5 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

Figure 2. Stick–slip generated ripples perpendicular to the sliding friction of polymer/metal under water lubrication. (a) Schematic of the friction between a polymer pin (8×8×20 mm3) and a 1Cr18Ni9Ti stainless steel plate specimen. (b) Friction force under 1 and 3 MPa and 9.42 mm/s for 6 s. (c) Wear surface topographies of the polymer pin after testing under 1 MPa and 9.42 mm/s for 3 min. (d and e) Cross-section profiles of the ripples of polymer pins after testing. (ΔT is the stick–slip period, Fpeak is the peak friction force, Δf is the decrease amplitude of the peak friction force, and ΔH and ΔL are the height and wave length of ripples, respectively.)

Effect of load and velocity on stick–slip phenomena and ripples. The stick–slip period increased slowly as the load increased, as shown in Figure 3(a). The peak friction force presented an approximately linear increase. The decrease amplitude of the peak friction force also increased linearly. Correspondingly, the ripples showed a similar principle with the friction force, as shown in Figure 3(b). The wave length of the ripples became slightly larger as the load increased, whereas the height increased linearly from 0.08 to 0.44 μm. Velocity had a considerable influence on the stick–slip phenomena. The stick–slip period of friction force decreased and followed a power function as the velocity increased from 2.6 s to 0.35 s, as shown in Figure 3(c). The peak friction force and


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 6 of 17

its decrease amplitude decreased drastically. The wave length and height of the ripples decreased as the velocity increased, as shown in Figure 3(d), and the decreasing tendency became slow as the velocity increased.

Figure 3. Stick–slip phenomena and ripples under different loads and velocities. (a) ΔT (see Figure 2(b)), Fpeak, and Δf of friction force at different loads. (b) ΔL (Figure 2(d)) and ΔH of ripples at different loads. (c) ΔT, Fpeak., and Δf of friction force at different velocities. (d) ΔL and ΔH of ripples at different velocities.

Effect of wear process on ripples. The surface topographies of the tested plastic pins at different test times (10, 30, 60, 90, 120, 150, and 180 s) under two velocities of 9.42 and 37.68 mm/s and 3 MPa were examined. The results are shown in Figure 4. Few perpendicular ripple areas were generated on the wear surface after the 10 s wear test under 9.42 mm/s and 3 MPa, as shown in Figure 4(a), and the ripples were non-obvious, non-continuous, and sparse. After testing for 90 s, the perpendicular ripple areas increased obviously, and the ripples were clearly seen. When the test time was extended to 180 s, many obvious, clear, and continuous perpendicular ripples distributed on the wear surface regularly and fully, as shown in Figure 4(c). Notably, the widths of the ripples were almost the same. In addition, the numbers of ripples on the entire wear surfaces on a reference line along the sliding direction were shown in Figure 4(d). The numbers increased linearly as the test time increased within 3 min under a load of 3 MPa and velocities of 9.42 and 37.68 mm/s, respectively. These phenomena revealed that the random contacts on


Page 7 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

the friction surfaces finally led to dense, clear, visible, continuous, and regular ripples.

Figure 4. Effects of test time on ripples of plastic pins under 3 MPa. (a), (b), and (c) show the SEM images of ripples under 3 MPa and 9.42 mm/s after testing for 10, 90, and 180 s, respectively. (d) shows the number of perpendicular ripples as a function of different test times under 9.42 and 37.68 mm/s.

The 3D surface topographies of perpendicular ripples belonging to 10, 90 and 180 s wear processes are shown in Figure 5. Many plastic materials were extruded and inclined along the sliding direction. Eventually, they exhibited serrated deformation, as shown in Figures 5(a) to 5(c). The cross sections of the ripples are shown in Figures 5(d) to 5(f). The lengths were almost the same, whereas the heights increased remarkably as the test time increased. Figure 5(g) shows the heights of the ripples increased following a power function of the test time under two velocities of 9.42 and 37.68 mm/s and 3 MPa, and increased slowly when the test time was long.


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 8 of 17

Figure 5. Effects of test time on ripples of plastic pins under 3 MPa. (a), (b), and (c) show the 3D wear surface topographies under 3 MPa and 9.42 mm/s after testing for 10, 90, and 180 s, respectively. (d), (e), and (f) show the cross sections of ripples. (g) shows the heights of the ripples as a function of different test times under 9.42 and 37.68 mm/s.

Relationship between deformation and friction force. The following process was proposed to occur during a stick–slip process, which is illustrated in Figure 6. The material on the wear surface of polymer pins experienced shear stresses due to adhesion friction force. The material was pulled and deformed along the sliding direction and eventually formed ripples during the stick–slip process. The maximum adhesion friction force needed to separate the random ripple (ripple i) and the 1Cr18Ni9Ti plate can be calculated using the following equation.[40] fipeak=Aiα+wiβ=aibiα+wiβ, ai=ΔLiλ,

(1) (2)

where fipeak is the max adhesion friction force between ripple i and the plate; α and β represent the coefficient determined by physical and mechanical properties, respectively; Ai is the real contact area; wi is the normal force


Page 9 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

for ripple i; ai and bi are the width and length of the contact zone between ripple i and metal, respectively; ΔLi is the wave length of ripple i; and λ is the contact width ratio between ripple i and metal, as shown in Figure 6(a). The highest pull force, Fist, of ripple i during the sticking process equals the max adhesion friction force fipeak between ripple i and the plate; Fist = fipeak. The pull force makes the ripple deform along the adhesion direction and can be calculated with the equation[41,42] Fist=aibiDik=fipeak,

(3)

where Di is the largest length of ripple i that could be stretched and deformed during a stick–slip process, as shown in Figure 6(a), and k is an equivalent constant that is related to the elastic modulus and Poisson’s ratio of the polymer. The height of the ripple ΔHi can be quantified in terms of percentage of elastic recovery (Δh) and stretching deformation. It can be calculated using the equation[43] ΔHi=Di(1−Δh).

(4)

Then, the relationship between adhesion friction force and ripple height can be attained using Equations (3) and (4). It follows that ΔHi= fipeak/(ΔLiλbiDik) (1−Δh),

(5)

fipeak/ΔHi=(1−Δh)/(ΔLiλbiDik).

(6)

(1−Δh)/(ΔLiλbiDik) is confirmed as a new constant of Ki, and it is related to the elastic modulus, Poisson’s ratio of the polymer, real contact area, and elastic recovery. Thus, for ripple i, Ki= fipeak/ΔHi.

(7)

The synthetic equivalent coefficient K of the wear surface of the polymer pin during the stick–slip process can be calculated using the following equation. K=K1+K2+...+Kn=f1peak/ΔH1+f2peak/ΔH2+...+fnpeak/ΔHn,

(8)

where K1, K2, ..., Kn are the constants of 1, 2, ..., n ripples, respectively; f1peak, f2peak, ..., fnpeak are the max adhesion friction forces between 1, 2, ..., n ripples and plate, respectively; and ΔH1, ΔH2, ..., ΔHn are the heights of 1, 2, ..., n ripples, respectively. The width and height of the ripples were almost the same, as shown in Figures 2(c), 2(d), and 2(e). Therefore, K=f1peak/ΔH1+f2peak/ΔH2+...+fnpeak/ΔHn=(f1peak+ f2peak+...+fnpeak) /ΔH= Fpeak/ΔH,

(9)

where ΔH is the average of the ripples and Fpeak is the total peak friction force during stick–slip, which can be measured as shown in Figure 2b.


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 10 of 17

Figure 6. Sketch of the formation of a ripple. (a) Tensile deformation and (b) plastic deformation models of a ripple during stick–slip.

Friction force determines the degree of tensile deformations of a polymer at the wear interface and eventually determines the geometry of the ripples. Figures 7(a) and 7(b) show the results of equivalent constant K at different loads and velocities. K was at a stable level of 200 N/μm in this work, indicating that the ripple heights increased linearly as the peak friction forces increased. The friction force was extremely low because of good lubrication performance and thick oil films under oil lubrication. Moreover, inducing regular ripples in polymer/metal friction was difficult. A dimensionless constant σ was defined as σ=(ΔT×v)/ΔL to characterize the ratio of sliding distance and wave length of the ripples during a stick–slip period, where v is the sliding velocity. σ fluctuated slightly at approximately 3,600 under different loads, as shown in Figure 7(c). Therefore, the wave length of the ripple increased linearly with the fluctuation period.[44,45] σ increased following a power function of velocity (see Figure 7(d)). These phenomena meant that a large sliding distance is required to induce ripples with the same wave length under high velocity.


Page 11 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

Figure 7. Relationship between friction force and ripple geometry. Results of Fpeak/ΔH at different (a) loads and (b) velocities. Results of ΔS/ΔL at different (c) loads and (d) velocities.

Effects of ripple on contact angle and COF of the polymer/metal. Test polymer pins with ripples were obtained with the abovementioned stick–slip method under water lubrication at 3 MPa and 9.42 mm/s. The wave length and height of ripples were approximately 5.2±0.6 μm and 0.44 ±0.07 μm, respectively. The effect of ripple on contact angle and COF as a surface texture was investigated, as shown in Figure 8. The ripple made the wetting contact angle increase by approximately 23° (from 63±1.9° to 86±2.5°), as shown in Figure 8(a). The contact angle hysteresis (difference between the advancing and receding contact angles) of the polymer surface with a ripple was smaller than that of the smooth surface, and the water drop could easily roll or slide on the ripple surface. These phenomena suggested that the ripples were useful for increasing the wetting contact angle.[46] As a kind of texture, the ripples could also help store lubricants, and improved the lubrication property when they slid against the metal plate under oil lubrication at 0.2 MPa and 37.7 mm/s as shown in Figure 8(b).[47] The average COF decreased by approximately 30% under low velocity, as shown in Figure 8(c). Moreover, the ripples decreased the average COF under low load, as shown in Figure 8(d).


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 12 of 17

Figure 8. Effects of ripple on contact angle and COF of the polymer/metal. (a) Contact angles of polymer pins with ripples and non-ripples. (b) Friction behaviors between the polymer pins with ripples and non-ripples sliding against metal under oil lubrication (oil: PAO 20) at 0.2 MPa and 37.7 mm/s. (c) The ripple affected the average COF under oil lubrication at different velocities and 0.2 MPa. (d) The ripple affected the average COF under oil lubrication at different loads and 37.7 mm/s.



CONCLUSION Stick–slip friction generated regular parallel ripples perpendicular to the sliding direction on a polymer surface

with different wave lengths and heights at different loads and velocities. The peak friction force during the sticking process linearly increased the ripple height. The ripple wave length, height, and stick–slip period decreased as the velocity increased, and the generated ripples improved the lubrication property under low loads and velocities. These results provide an improved understanding of the stick–slip phenomenon and can be developed into a novel


Page 13 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

surface patterning method for polymer application. This process offers a potential to generate regular ripples in 0.1–10 μm features over an area of square centimeters, which is interesting due to potential applications in reducing COF, hydrophobic surfaces, and diffraction gratings.



ACKNOWLEDGE This work is supported by the National Natural Science Foundation of China (Grant Nos. 51605248, and

51425502), Hubei Provincial Natural Science Foundation of China (2018CFB130) and Fundamental Research Funds for the Central Universities (WUT: 2018IVA056).



REFERENCE

(1) Wen, Y. C.; Zha, S.; Liu, X.; Yang, S. S.; Guo, P.; Shi, G. S.; Fang, H. P.; Shen, Y. R.; Tian, C. S. Unveiling Microscopic Structures of Charged Water Interfaces by Surface-Specific Vibrational Spectroscopy. Phys. Rev. Lett., 2016, 116, 016101. (2) Osawa, S.; Yabe, M.; Miyamura, M.; Mizuno, K. Preparation of Super-hydrophobic Surface on Biodegradable Polymer by Transcribing Microscopic Pattern of Water-repellent Leaf. Polymer, 2006, 47, 11, 3711–3714. (3) D’Acunto, M.; Dinelli, F.; Pingue, P. Nanoscale Rippling on Polymer Surfaces Induced by AFM Manipulation. Beilstein J. Nanotechnol., 2015, 6, 1, 2278–2289. (4) Watson, J. A.; Brown, C. L.; Myhra, S.; Watson, G. S. Two-dimensional Stick–slip on a Soft Elastic Polymer: Pattern Generation Using Atomic Force Microscopy. Nanotechnology, 2006, 17, 10, 2581–9. (5) Pettersson, U.; Jacobson, S. Influence of Surface Texture on Boundary Lubricated Sliding Contacts. Tribol. Int., 2003, 36, 11, 857–864. (6) Boningari, T.; Ettireddy, R. P.; Somogyvari, A.; Liu, Y.; Vorontsov, A.; McDonald, C. A.; Smirniotis, P. G. Influence of Elevated Surface Texture Hydrated Titania on Ce-doped Mn/TiO2 Catalysts for the Low-temperature SCR of NOxunder Oxygen-rich Conditions. J. Catal., 2015, 325, 145–155. (7) Jones, P. R.; Elliott, A. R.; Patankar, N. A. Sustaining Superheated Liquid within Hydrophilic Surface Texture. Langmuir, 2016, 32, 48, 12947–12953. (8) Do, M. T.; Tang, Z. M.; Kane, F. D. Evolution of Road-surface Skid-resistance and Texture due to Polishing. Wear, 2009, 266, 5–6, 574–577. (9) Senin, T. N.; Blunt, L.; Leach, R. K.; Taylor, J. S. J. Surface Texture Metrology for Metal Additive Manufacturing: a Review. Pr. Eng. Man-Gt., 2016, 46, 34–47.


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 14 of 17

(10) Abouelatta, O. B.; Mádl, J. Surface Roughness Prediction Based on Cutting Parameters and Tool Vibrations in Turning Operations. J. Mater. Process. Tech., 2001, 118, 1–3, 269–277. (11) Shokrani, A.; Dhokia, V.; Newmanl, S. T. Investigation of the Effects of Cryogenic Machining on Surface Integrity in CNC end Milling of Ti–6Al–4V Titanium Alloy. J. Manuf. Process., 2016, 21, 172–179. (12) Kaynak, Y.; Lu, T.; Jawahir, I. Cryogenic Machining-induced Surface Integrity: A Review and Comparison with Dry, MQL, and Flood-cooled Machining. Mach, Sci, Technol., 2014, 18, 2, 149–198. (13) Pusavec, F.; Kopac, J. Achieving and Implementation of Sustainability Principles in Machining Processes. J. Adv. Prod. Eng. Manage., 2009, 3–4, 58–69. (14) Brandl, E.; Heckenberger, U.; Holzinger, V.; Buchbinder, D. Additive Manufactured AlSi10Mg Samples Using Selective Laser Melting (SLM): Microstructure, High Cycle Fatigue, and Fracture Behavior. Mater. Des., 2012, 34, 159–169. (15) Everton, S. K.; Hirsch, M.; Stravroulakis, P.; Leach, R. K.; Clare, A. T. Review of In-situ Process Monitoring and In-situ Metrology for Metal Additive Manufacturing. Mater. Des., 2016, 95, 431–445. (16) Puertas, T. I.; Luis, C. J. J. Modelling of Surface Finish, Electrode Wear and Material Removal Rate in Electrical Discharge Machining of Hard-to-machine Alloys. Pr. Eng. Man-Gt., 2015, 40, 33–45. (17) Lacalle, L. D.; Lamikiz, L. N.; Sanchez, A.; Arana, J. A. J. Mater. Improving the Surface Finish in High Speed Milling of Stamping Dies. Process. Tech., 2002, 123, 292–302. (18) Mao, K.; Langlois, P.; Hu, Z.; Alharbi, K.; Xu, X.; Milson, M.; Li, W.; Hooke, C. J.; Chetwynd, D. The Wear and Thermal Mechanical Contact Behaviour of Machine Cut Polymer Gears. Wear, 2015, 332–333, 822–826. (19) Jamshidinia, M. Kovacevic, R. The Influence of Heat Accumulation on the Surface Roughness in Powder-bed Additive Manufacturing. Surf. Topogr. Metrol. Prop., 2015, 3, 014003. (20) Formica, G.; Talò, M.; Lacarbonara, W. Nonlinear Modeling of Carbon Nanotube Composites Dissipation due to Interfacial Stick–slip. Int. J. Plasticity, 2014, 53, 148–163. (21) Dong, C. L.; Shi, L. C.; Li, L. Z.; Bai, X. Q.; Yuan, C. Q.; Tian, Y. Stick-slip Behaviours of Water Lubrication Polymer Materials under Low Speed Conditions. Tribol. Int., 2017, 106, 55–61. (22) Lee, D. W.; Banquy, X.; Israelachvili, J. N. Stick-slip Friction and Wear of Articular Joints. Proc. Natl. Acad. Sci., 2013, 110, 7, E567–E574. (23) Karnopp, D.; Dyn. J. Computer Simulation of Stick-Slip Friction in Mechanical Dynamic Systems. Syst. Trans. ASME, 1985, 107, 1, 100–103. (24) Galvanetto, U.; Bishop, S. R.; Briseghella, L. Mechanical Stick-slip Vibrations. Int. J. Bifurcat. Chaos, 1995, 5,


Page 15 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

3, 637–651. (25) Dong, C. L.; Yuan, C. Q.; Bai, X. Q.; Qin, H. L.; Yan, X. P. Investigating Relationship between Deformation Behaviors and Stick-slip Phenomena of Polymer Material. Wear, 2017, 376–377, 1333-1338. (26) Tian, Y.; Pesika, N.; Zeng, H.; Rosenberg, K.; Zhao, B.; Mcguiggan, P. Adhesion and Friction in Gecko Toe Attachment and Detachment. P. Natl. Acad. Sci. USA, 2006, 103, 51, 19320–19325. (27) Majumdar, A.; Butola, B. S.; Srivastava, A. An Analysis of Deformation and Energy Absorption Modes of Shear Thickening Fluid Treated Kevlar Fabrics as Soft Body Armour Materials. Mater. Design, 2013, 51, 5, 148–153. (28) Maegawa, S.; Nakano, K. Mechanism of Stick-slip Associated with Schallamach Waves. Wear, 2010, 268, 7, 924–930. (29) Ryou, H.; Chung, K. Development of Viscoelastic/rate-sensitive-plastic Constitutive Law for Fiber-reinforced Composites and its Applications Part II: Numerical Formulation and Verification. Compos. Sci. Technol., 2009, 69, 2, 292–299. (30) Dong, C. L.; Yuan, C. Q.; Bai, X. Q.; Yan, X. P.; Peng, Z. X. Study on Wear Behavior and Wear Model of Nitrile Butadiene Rubber under Water Lubricated Conditions. RSC Adv., 2014, 4, 19034–19042. (31) Zeng, H. B.; Huang, J.; Tian, Y.; Li, L.; Tirrell, M. V.; Israelachvili, J. N. Adhesion and Detachment Mechanisms between Polymer and Solid Substrate Surfaces: using Polystyrene–mica as a Model System. Macromolecules, 2016, 49, 14, 5223–5231. (32) Dong, C. L.; Yuan, C. Q.; Bai, X. Q.; Yan, X. P.; Peng, Z. Tribological Properties of Aged Nitrile Butadiene Rubber under Dry Sliding Conditions. Wear, 2015, 322-323, 226–237. (33) Gauthier, C.; Lafaye, S.; Schirrer, R. Elastic Recovery of a Scratch in a Polymeric Surface: Experiments and Analysis. Tribol. Int., 2001, 34, 7, 469–479. (34) Viswanathan, K.; Sundaram, N. K. Distinct Stick-slip Modes in Adhesive Polymer Interfaces. Wear, 2017, 376–377, 1271–1278. (35) Gao, X.; Wang, K. Strength of Stick-slip and Creeping Subduction Megathrusts from Heat Flow Observations. Science, 2014, 345, 1038–1041. (36) Jiang, H.; Zhang, J. W.; Kang, G. Z.; Xi, C. C.; Jiang, C. K.; Liu, Y. J. A Test Procedure for Separating Viscous Recovery and Accumulated unrecoverable Deformation of Polymer under Cyclic Loading. Polym. Test., 2013, 32, 8, 1445–1451. (37) Dong, C. L.; Yuan, C. Q.; Wang, L.; Liu, W.; Bai, X. Q.; Yan, X. P. Tribological Properties of Water-lubricated


Langmuir 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Page 16 of 17

Rubber Materials after Modification by MoS2 Nanoparticles. Sci. Rep., 2016, 6, 35023. (38) Schallamach, A. Friction and Abrasion of Rubber. Wear, 1958, 1, 5, 384–417. (39) Maegawa, S.; Itoigawa, F.; Nakamura, T. Dynamics in Sliding Friction of Soft Adhesive Elastomer: Schallamach Waves as a Stress-relaxation Mechanism. Tribol. Int., 2016, 96: 23–30. (40) Tao, D.; Gao, X.; Lu, H.; Liu, Z.; Li, Y.; Tong, H.; Tian, Y. Controllable Anisotropic Dry Adhesion in Vacuum: Gecko Inspired Wedged Surface Fabricated with Ultraprecision Diamond Cutting. Adv. Funct. Mater., 2017, 27, 1606576, 1–9. (41) Ryschenkow, G.; Arribart, H. Adhesion Failure in the Stick-Slip Regime: Optical and AFM Characterizations and Mechanical Analysis. J. of Adhesion, 2006, 58, 1–2, 143–161. (42) Jiang, H.; Browning, R.; Sue, H. J. Understanding of Scratch-induced Damage Mechanisms in Polymers. Polymer, 2009, 50, 16, 4056–4065. (43) Hadal, R. S.; Misra, R. D. K. Scratch Deformation Behavior of Thermoplastic Materials with Significant Differences in Ductility. Mater. Sci. Eng. A, 2005, 398, 1–2, 252–261. (44) Park, J. S.; Lee, S. M.; Joo, B. S.; Jang, H. The Effect of Material Properties on the Stick–slip Behavior of Polymers: A Case Study with PMMA, PC, PTFE, and PVC. Wear, 2017, 378–379, 11–16. (45) Kligerman, Y.; Varenberg, M. Elimination of Stick-slip Motion in Sliding of Split or Rough Surface. Tribol. Lett., 2014, 53, 2, 395–399. (46) Singh. B.; Janajreh, Isam.; Hashaikeh, Raed. A Facile Approach to Fabricate Superhydrophobic Membranes with Low Contact Angle Hysteresis. J. Membrane Sci., 2017, 539, 144–151. (47) Gachot, C.; Rosenkranz, A.; Hsu, S. M.; Costa, H. L. A Critical Assessment of Surface Texturing for Friction and Wear Improvement. Wear, 2017, s372–373, 21–41.


Page 17 of 17 1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

Langmuir

For Table of Contents Use Only


Rippled polymer surface generated by stick-slip friction - Langmuir

Recommend Documents