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A large number of practices have shown that under the coupling influence of complex working conditions and frequent reciprocating contact, the surfaces of semiconductor devices in micro/nano electromechanical systems often produce adhesive wear, which is the essential reason resulting in short durability service life and declining contact mechanical properties for microelectronics semiconductor devices. However, graphene can significantly improve the interface properties of mechanical components and electronic components due to its excellent mechanical properties, such as high carrier concentration, good thermal conductivity, and low shear. Thus, the study of mechanical strengthening properties and plastic deformation of SiC material with covered multi-layer graphene in MEMS devices will play a significant role in improving the durability service life of MEMS device, and understanding its strengthening and toughening mechanism. Therefore, this paper studies and discusses the effects of stacking type and extreme service temperature with low and high levels on the contact mechanical properties (maximum load, hardness, Young modulus, contact stiffness), micro-structure evolution, contact mass, fold morphology, and total length of dislocation. The atomic-scale mechanism of enhanced mechanical properties of SiC material with multi-layer graphene is explained. The research shows that the damage to carbon-carbon bond at the maximum indentation depth will lead graphene to lose the excellent in-plane elastic deformation capability when the graphene stacking type is AB stacking, so that the maximum load-bearing capacity of the substrate covered by three layers of graphene will drop linearly. In addition, the mechanical property of SiC material coated with three graphene layers is twice that of pure SiC substrate, and the strengthening mechanism is mainly due to the increase of wrinkle caused by the increase of multilayer graphene loading, which causes the quality of contact between the SiC substrate and the virtual indenter to decrease, thus increasing the interface contact stiffness. The increase of the active temperature will trigger off the increase of the atomic vibration frequency, which will cause the number of interface contact atoms to increase greatly, and the interface contact stiffness will weaken, and finally lead the interface contact quality to improve, This is because the mechanical properties of SiC substrate coated with multilayer graphene will decrease approximately linearly with the extreme service from low temperature to high temperature. In addition, the stress concentration in the subsurface layer of SiC substrate can induce the evolution of its micro-structure, and the increase of the number of graphene layers on the substrate can effectively reduce the stress concentration distribution in the subsurface layer of the substrate.
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Keywords:
- SiC material /
- multilayer graphene /
- mechanical strengthening /
- molecular dynamic method /
- contact stiffness
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图 1 SiC基底覆多层石墨烯薄膜的分子动力学模型
Figure 1. Molecular dynamics model of SiC substrate coated with multilayer graphene films.
图 2 SiC基底覆多层石墨烯的载荷与位移曲线关系
Figure 2. Relation between load and displacement curve of SiC substrate coated with multilayer graphene.
图 3 SiC基底覆多层石墨烯最大压深时的最大承载荷 (a) AA堆垛; (b) AB堆垛
Figure 3. Maximum load bearing capacity of SiC substrate coated with multilayer graphene at the maximum pressing depth: (a) AA stack; (b) AB stack.
图 4 SiC基底覆多层石墨烯的表面形貌受温度和石墨烯堆垛类型影响
Figure 4. Surface morphology of multi-layer graphene coated with SiC substrate is affected by temperature and graphene stacking type.
图 5 SiC基底覆多层石墨烯受载产生的剪切变形受温度和石墨烯堆垛类型影响
Figure 5. Shear deformation of SiC substrate coated with multilayer graphene under load is affected by the temperature and the type of graphene stacking.
图 6 SiC基底覆石墨烯层数的微结构演化和位错总长随使役温度的影响变化
Figure 6. Effect of service temperature change on microstructure evolution and dislocation length of SiC substrate with multilayer graphene coated.
图 7 SiC基底覆石墨烯层数的力学性能量化分析
Figure 7. Quantitative analysis of mechanical properties of SiC substrate coated with graphene layers.
图 8 SiC基底覆三层石墨烯的接触刚度随使役温度变化的影响
Figure 8. Influence of the contact stiffness of SiC substrate coated with three layers of graphene with the change of service temperature.
图 9 使役温度和石墨烯堆垛类型对界面接触质量分布影响
Figure 9. Effect of service temperature and graphene stacking type on interface contact mass distribution.
图 10 石墨烯堆垛类型对石墨烯和SiC基底的应力分布影响
Figure 10. Effect of graphene stacking type on stress distribution of graphene and SiC substrates.
表 1 SiC基底与石墨烯间的L-J势参数值与第一性原理计算验证
Table 1. L-J potential parameter values and first principles calculation verification between SiC substrate and graphene.
Force description $ \sigma $/nm(MD) $ \varepsilon $/ eV(MD) $ \varepsilon $/ eV(DFT) C—Si 0.4073 0.008906989 0.00884012 C—C 0.3851 0.00455323 0.00461245 
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[1] Woodilla D, Buonomo M, Bar-On I, Katz R N, Whalen T 1993 J. Am. Chem. Soc. 76 249
Google Scholar
[2] Talwar D N, Sherbondy J C 1995 Appl. Phys. Lett. 67 3301
Google Scholar
[3] Demenet J L, Amer M, Tromas C 2013 Phy. Status Solidi 10 64
Google Scholar
[4] Miranda A, Cuevas J L, Ramos A E, Cruz-Irisson M 2009 Microelectron. J. 40 796
Google Scholar
[5] Wang G B, Lei Y Z 2005 Prog. Nat. Sci. 10 571
Google Scholar
[6] Sakhaee A 2009 Solid State Commun. 149 91
Google Scholar
[7] Morozov S V, Novoselow K S, Katsnelson M I 2008 Phys. Rev. Lett. 100 016602
Google Scholar
[8] Balandin A A, Ghosh S, Bao W 2008 Nano Lett. 8 902
Google Scholar
[9] Tang Y L, Peng P, Wang S Y 2017 Chem. Mater. 29 8404
Google Scholar
[10] Li S Z, Li Q Y, Carpick R W 2016 Nature 539 541
Google Scholar
[11] Wang S Y, Han S B, Xin G Q 2018 Mater. Design 139 181
Google Scholar
[12] Xu K, Duan X Y, L Y 2020 J. Exp. Nanosci. 15 417
Google Scholar
[13] Miyoshi K, Buckley D H, Srinivasan M 1983 Am. Ceram. Soc. Bull. 62 454
[14] Tapasztó O, Tapasztó L, Markò M 2011 Chem. Phys. Lett. 511 340
Google Scholar
[15] Li Q, Zhang Y, Gong H 2015 Ceram. Int. 41 13547
Google Scholar
[16] Kun P, Tapasztó O, Wéber F 2012 Ceram. Int. 38 211
Google Scholar
[17] Shin J H, Hong S H 2014 J. Eur. Ceram. Soc. 34 1297
Google Scholar
[18] Dusza J, Morgiel J, Duszová A 2012 J. Eur. Ceram. Soc. 32 3389
Google Scholar
[19] Nieto A, Bisht A, Lahiri D L 2017 Int. Mater. Rev. 62 241
Google Scholar
[20] 李炯利, 王旭东, 武岳, 曹振, 郭建强, 张海平 2018 稀有金属 42 252
Li J L, Wang X D, Wu Y, Cao Z, Guo J Q, Zhang H P 2018 Chin. J. Rare Metals 42 252
[21] Nawaz A, Islam B, Mao W G, Lu C S, Shen Y G 2019 Int. J. Appl. Ceram. Tec. 16 706
Google Scholar
[22] Zhao K, Aghababaei R 2020 Phys. Rev. Mater. 4 103605
Google Scholar
[23] Juan C C, Tsai M H, Tsai C W, Hsu W L, Lin C M, Chen S K, Lin S J, Yeh J W 2016 Mater. Lett. 184 200
Google Scholar
[24] Subin L, Aviral V, Jiseong I, Kim B, Sang H O 2020 Nat. Comm. 11 2367
Google Scholar
[25] Wang J, Zhang X, Fang F, Chen R 2018 Appl. Sur. Sci. 455 608
Google Scholar
[26] Zhao L, Zhang J J, Janine P, Alam M, Hartmaier A 2021 Mater. Design 197 109223
Google Scholar
[27] Kondo S, Koyanagi T, Hinoki T 2014 J. Nucl. Mater. 448 487
Google Scholar
[28] Zhao S, Flanagan R, Hahn E N, Kad B, Remington B A, Wehrenberg C E, Cauble R, More K 2018 Acta Mater. 158 206
Google Scholar
[29] Branicio P S, Kalia R K, Nakano A, Vashishta P 2010 Appl. Phys. Lett. 97 111903
Google Scholar
[30] Xiang H G, Li H T, Fu T 2017 Acta Mater. 138 131
Google Scholar
[31] Guo J, Chen J J, Wang Y Q 2020 Ceram. Int. 46 12686
Google Scholar
[32] Xiang H G, Guo W L 2022 Int. J. Plasticity 150 103197
Google Scholar
[33] Xiang H G, Guo W L 2022 Acta Mech. Sin. 38 121451
Google Scholar
[34] Oliver W C, Pharr G M 2011 J. Mater. Res. 7 1564
[35] Fan X, Rui Z, Cao H, Fu R, Feng R, Yan C 2019 Materials 12 770
Google Scholar
[36] Oliver W C, Pharr G M 2011 J. Mater. Res. 19 3
Google Scholar
[37] Chen J J, Wu H, Bai S H 2023 Mat. Sci. Semicon. Proc. 165 107651
Google Scholar
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