1 s2.0 S0021979718302352 Main
1 s2.0 S0021979718302352 Main
1 s2.0 S0021979718302352 Main
Regular Article
g r a p h i c a l a b s t r a c t
a r t i c l e i n f o a b s t r a c t
Article history: In this work, a flexible resistive switching memory device based on ZnO film was fabricated using a fold-
Received 25 January 2018 able Polyethylene terephthalate (PET) film as substrate while Ag and Ti acts top and bottom electrode.
Revised 24 February 2018 Our as-prepared device represents an outstanding nonvolatile memory behavior with good ‘‘write–rea
Accepted 1 March 2018
d–erase–read” stability at room temperature. Finally, a physical model of Ag conductive filament is con-
Available online 2 March 2018
structed to understanding the observed memory characteristics. The work provides a new way for the
preparation of flexible memory devices based on ZnO films, and especially provides an experimental basis
Keywords:
for the exploration of high-performance and portable nonvolatile resistance random memory (RRAM).
ZnO film
PET substrate
Ó 2018 Elsevier Inc. All rights reserved.
Flexible
Nonvolatile
Memory device
⇑ Corresponding authors at: School of Physical Science and Technology, Southwest Jiaotong University, Chengdu, Sichuan 610031, China.
E-mail addresses: bsun@swjtu.edu.cn (B. Sun), ydxia@swjtu.edu.cn (Y. Xia).
1
These authors contributed equally to this work.
https://doi.org/10.1016/j.jcis.2018.03.001
0021-9797/Ó 2018 Elsevier Inc. All rights reserved.
20 B. Sun et al. / Journal of Colloid and Interface Science 520 (2018) 19–24
1. Introduction
tance state (HRS) and a low resistance state (LRS) under the
applied voltage [9,10]. If the HRS is defined as logic ‘‘0”, the LRS
holes. Cross section condition of device was characterized using
is defined as logic ‘‘1”, thus the switching phenomenon can be
SEM. The element composition of as-prepared films was observed
applied for the storage of information, the switching cell through
by energy dispersive X-ray spectroscopy (EDX). The memory char-
proper process can be used for preparing of memory device
acteristics of devices were measured using a workstation (CHI-
[11,12].
660E) at room temperature. The corresponding test circuit is
In many current reports, researchers have found that many
shown in Fig. 3b.
semiconductor and insulator materials exhibit resistive switching
memory behavior [13–15]. ZnO has many advantages, such as sim-
ple chemical composition, rich reserves, high transparency, non- 3. Results and discussion
toxicity, and so on. Therefore, ZnO has been widely used for
preparing many kinds of optoelectronic devices [16–18]. Recently, Fig. 2a shows the EDX spectra of as-prepared ZnO film on Ti bot-
the RRAM memories based on ZnO has also been reported [19–21]. tom electrode, confirming that as-prepared product is composed of
In particular, the fixable electronic devices are very useful because two elements (Zn and O) without any other impurities, which is
of the convenience of carrying and deformable [22]. In the prepa- pure ZnO according to the atomic ratio (1:1) of the elements from
ration of flexible electronic devices, PET is commonly used as sub- the inset to Fig. 2a. Among the Ti peaks are because of the used Ti
strate because of PET has a lot of advantages, such as excellent bottom electrode. Fig. 2b exhibits the cross-sectional FESEM image
physical and mechanical properties in a wide temperature range, of as-prepared device, we can see that a thickness of about 400 nm
high thermal stability, good electrical insulation, high creep resis- of ZnO film layer was deposited on the Ti bottom electrode. It can
tance and fatigue resistance, and good dimensional stability, and be observed that the multilayer films are relatively smooth, and
so on [23,24]. In addition, PET is nontoxic, tasteless and safety for there is an obvious interface between adjacent layers. The ideal
practical applications [25]. device structure is the key to further study its performance. The
In our work, in order to preparing a fixable resistive switching inset in Fig. 2b shows the optical photograph of the device. From
memory device, we use a fixable PET film as substrate. Ti film the above results, we can confirm that the as-prepared device is
was firstly sputtered on PET substrate by a magnetron sputtering qualified.
equipment, Ti as bottom electrode can further reduce the bending Fig. 3a display the photograph of the as-prepared memory
stiffness and strain, thus the as-prepared product can reduce the device, indicating an excellent bending stability and a great poten-
fatigue caused by the curling. The detail preparation process of tial for nonvolatile memory applications in flexible electronics. The
resistive switching memory device is shown in Fig. 1. Through fur- electrical performances is tested by the experimental test circuit
ther study, we found that the device with Ag/ZnO/Ti/PET structure shown in Fig. 3b under a scanning rate of 0.1 V ms1, resulting dis-
display an excellent resistive switching memory characteristic. play Ag/ZnO/Ti/PET device holds a resistive switching memory
Therefore, our device has the capability to work as a fixable mem- behavior. In the test process, we set up the compliance current
ory device, combination that opens the door to novel multifunc- (CC) of 10 mA for avoid electrical permanent breakdown during
tional fixable and wearable electronic devices. the test process. The sweeping directions of applied voltage are
from 0 ? 2.0 V ? 0 ? 2.0 V ? 0. The positive pole of the power
supply is connected to the top electrode of the device, the linear
2. Materials and methods I-V curves exhibiting an almost symmetrical hysteresis behavior
(Fig. 3c). This kind of I–V characteristic is termed resistive switch-
Fig. 1 schematically illustrates the fabrication process of Ag/ ing memory behavior, indicating the Ag/ZnO/Ti/PET memory
ZnO/Ti/PET structure device. Our device was fabricated by a mag- device exhibited a bipolar switching mode, which can provide a
netron sputtering equipment, the vacuum degree of the deposited most clear memory window when under read and write voltage.
film is 5 105 Pa and the working pressure of Ar is 0.5 Pa. the Ti The memory window is a key technical parameter for resistive
bottom electrode and ZnO thin film were orderly grown on a PET switch memory devices, which should provide different logic
substrate. Finally, the Ag top electrode (the thickness of 500 states for writing and reading data [26,27]. The corresponding log-
nm) was deposited by using a metal shadow mask with small arithmic I–V curves is exhibited in Fig. 3d. Application of a positive
B. Sun et al. / Journal of Colloid and Interface Science 520 (2018) 19–24 21
Fig. 2. (a) EDX spectrum of ZnO film grown bottom electrode Ti, the inset shows Zn/O atomic ratios. (b) The cross-sectional FESEM image of our device.
Fig. 3. (a) The photograph of the as-prepared memory device. (b) The experimental test circuit. (c) The current-voltage (I-V) characteristics curve of Ag/ZnO/Ti/PET device
structure. (d) The corresponding logarithmic I–V curves.
voltage on Ag top electrode can switch the memory device from showing non-noticeable degradation after 200 switching cycles.
the HRS state to the LRS state at 1.45 V, which was defined as The resistance ratio is about 10 through appropriate calculations,
the ‘‘Set” process. Afterward, the device returned to the HRS state illustrating that the memory performance are outstanding with
when a reverse bias (1.5 V) was applied, which was called the larger memory window. According to the above observed results,
‘‘Reset” process, demonstrating the great potential of Ag/ZnO/Ti/ the nonvolatile memory behavior in Ag/ZnO/Ti/PET device pro-
PET device for nonvolatile memory applications. The above data vides the potential application value in fixable and wearable elec-
fully demonstrate the great non-volatile memory potential Ag/ tronic systems. Fig. 4b exhibits the bar graph of the HRS/LRS
ZnO/Ti/PET device in practical memory applications. resistance ratio and the thickness of the ZnO film. The dependence
Indeed, for the practical application of the resistive switching between the HRS/LRS resistance ratio and the thickness of the ZnO
memory, the HRS/LRS resistance ratio is an pivotal parameter film can be observed, in which the as-prepared devices display a
[28,29]. The resistance ratio of Ag/ZnO/Ti/PET devices under maximum HRS/LRS resistance ratio (10) when the thickness of
applied bias voltage of 0.4 V were depicted, as shown in Fig. 4a, the ZnO layer is reached to about 400 nm.
22 B. Sun et al. / Journal of Colloid and Interface Science 520 (2018) 19–24
Fig. 5. (a) The I–V curves in log–log scale for Ag/ZnO/Ti/PET structure in the positive voltage case, the scatterer is the data obtained by the experiment, and the straight line is
the curve fitted by the theoretical model. (b) Region I in the HRS. (c) Region II in the HRS. (d) Region III in the LRS.
References
[11] Y. Sun, J. Lu, C. Ai, D. Wen, X. Bai, Multilevel resistive switching and nonvolatile [27] K.J. Yoon, S.J. Song, J.Y. Seok, J.H. Yoon, T.H. Park, D.E. Kwon, C.S. Hwang,
memory effects in epoxy methacrylate resin and carbon nanotube composite Evolution of the shape of the conducting channel in complementary resistive
films, Org. Electron. 32 (2016) 7. switching transition metal oxides, Nanoscale 6 (2014) 2161.
[12] L. Gao, Y. Li, Q. Li, Z. Song, F. Ma, Enhanced resistive switching characteristics in [28] B. Sun, H. Li, L. Wei, P. Chen, Hydrothermal synthesis and resistive switching
Al2O3 memory devices by embedded Ag nanoparticles, Nanotechnology 28 behavior of WO3/CoWO4 core–shell nanowires, CrystEngComm 16 (2014) 9891.
(2017) 215201. [29] J. Kolar, J.M. Macak, K. Terabe, T. Wagner, Down-scaling of resistive switching
[13] B. Sun, L. Wei, H. Li, X. Jia, J. Wu, P. Chen, The DNA strand assisted conductive to nanoscale using porous anodic alumina membranes, J. Mater. Chem. C 2
filament mechanism for improved resistive switching memory, J. Mater. Chem. (2014) 349.
C 3 (2015) 12149. [30] S.-T. Han, Y. Zhou, B. Chen, C. Wang, L. Zhou, Y. Yan, J. Zhuang, Q. Sun, H. Zhang,
[14] G. Zhou, B. Sun, Y. Yao, H. Zhang, A. Zhou, K. Alameh, B. Ding, Q. Song, V.A.L. Roy, Hybrid flexible resistive random access memory-gated transistor
Investigation of the behavior of electronic resistive switching memory based for novel nonvolatile data storage, Small 12 (2016) 390.
on MoSe2-doped ultralong Se microwires, Appl. Phys. Lett. 109 (2016) 143904. [31] J. Lee, W.G. Hong, H. Lee, Non-volatile organic memory effect with thickness
[15] C. Li, B. Gao, Y. Yao, X. Guan, X. Shen, Y. Wang, P. Huang, L. Liu, X. Liu, J. Li, C. control of the insulating LiF charge trap layer, Org. Electron. 12 (2011) 988.
Gu, J. Kang, R. Yu, Direct observations of nanofilament evolution in switching [32] S. Sivaramakrishnan, P.J. Chia, Y.C. Yeo, L.I. Chua, P.K. Ho, Controlled insulator-
processes in HfO2-based resistive random access memory by in situ TEM to-metal transformation in printable polymer composites with nanometal
studies, Adv. Mater. 29 (2017) 1602976. clusters, Nat. Mater. 6 (2007) 149.
[16] S.K. Kumar, S. Murugesan, S. Suresh, S.P. Raj, CuO thin films made of nanofibers [33] T. Tsuruoka, I. Valov, S. Tappertzhofen, Jan van den Hurk, T. Hasegawa, R.
for solar selective absorber applications, Sol. Energy 94 (2013) 299. Waser, M. Aono, Redox reactions at Cu,Ag/Ta2O5 interfaces and the effects of
[17] D. Bi, G. Boschloo, S. Schwarzmuller, L. Yang, E.M.J. Johansson, A. Hagfeldt, Ta2O5 film density on the forming process in atomic switch structures, Adv.
Efficient and stable CH3NH3PbI3-sensitized ZnO nanorod array solid-state solar Funct. Mater. 25 (2015) 6374.
cells, Nanoscale 5 (2013) 11686. [34] Y. Sharma, P. Misra, S.P. Pavunny, R.S. Katiyar, Multilevel unipolar resistive
[18] S.A. Vanalakar, V.L. Patil, N.S. Harale, S.A. Vhanalakar, M.G. Gang, J.Y. Kim, P.S. memory switching in amorphous SmGdO3 thin film, Appl. Phys. Lett. 104
Patil, J.H. Kim, Controlled growth of ZnO nanorod arrays via wet chemical (2014) 073501.
route for NO2 gas sensor applications, Sens. Actuators B Chem. 221 (2015) [35] S.M. Sze, Physics of Semiconductor Devices, Wiley, New York, 1981.
1195. [36] D.I. Son, T.W. Kim, J.H. Shim, J.H. Jung, D.U. Lee, J.M. Lee, W.I. Park, W.K. Choi,
[19] Y. Huang, Z. Shen, Y. Wu, X. Wang, S. Zhang, X. Shi, H. Zeng, Amorphous ZnO Flexible organic bistable devices based on graphene embedded in an insulating
based resistive random access memory, RSC Adv. 6 (2016) 17867. poly (methyl methacrylate) polymer layer, Nano Lett. 10 (2010) 2441.
[20] F.-C. Chiu, P.-W. Li, W.-Y. Chang, Reliability characteristics and conduction [37] J. Lin, D. Ma, Origin of negative differential resistance and memory
mechanisms in resistive switching memory devices using ZnO thin films, characteristics in organic devices based on tris (8-hydroxyquinoline)
Nanoscale Res. Lett. 7 (2012) 178. aluminum, J. Appl. Phys. 103 (2008) 124505.
[21] Y.H. Kang, J.-H. Choi, T.I. Lee, W. Lee, J.-M. Myoung, Thickness dependence of [38] B. Zhang, M. Fraenkl, J.M. Macak, T. Wagner, Ag filament and surface particle
the resistive switching behavior of nonvolatile memory device structures formation in Ag doped AsS2 thin film, Mater. Lett. 163 (2016) 4.
based on undoped ZnO films, Solid State Commun. 151 (2011) 1739. [39] E. Yoo, M. Lyu, J.-H. Yun, C. Kang, Y. Choi, L. Wang, Bifunctional resistive
[22] J. Lee, A.J.J.M. van Breemen, V. Khikhlovskyi, M. Kemerink, R.A.J. Janssen, G.H. switching behavior in an organolead halide perovskite based Ag/CH3NH3PbI3-
Gelinck, Pulse-modulated multilevel data storage in an organic ferroelectric xClx/FTO structure, J. Mater. Chem. C 4 (2016) 7824.
resistive memory diode, Sci. Rep. 6 (2016) 24407. [40] K. Krishnan, M. Aono, T. Tsuruoka, Kinetic factors determining conducting
[23] Z. Ma, M. Kotaki, T. Yong, W. He, S. Ramakrishna, Surface engineering of filament formation in solid polymer electrolyte based planar devices,
electrospun polyethylene terephthalate (PET) nanofibers towards Nanoscale 8 (2016) 13976.
development of a new material for blood vessel engineering, Biomaterials 26 [41] S.K. Vishwanath, J. Kim, Resistive switching characteristics of all-solution-
(2005) 2527. based Ag/TiO2/Mo-doped In2O3 devices for non-volatile memory applications,
[24] W. Qiu, U.W. Paetzold, R. Gehlhaar, V. Smirnov, H.-G. Boyen, J.G. Tait, B. J. Mater. Chem. C 4 (2016) 10967.
Conings, W. Zhang, C.B. Nielsen, I. McCulloch, L. Froyen, P. Heremans, D. [42] E.D. Mauro, O. Carpentier, S.I. Yáñez Sánchez, N. Ignoumba Ignoumba, M.
Cheyns, An electron beam evaporated TiO2 layer for high efficiency planar Lalancette-Jean, J. Lefebvre, S. Zhang, C.F.O. Graeff, F. Cicoira, C. Santato,
perovskite solar cells on flexible polyethylene terephthalate substrates, J. Resistive switching controlled by the hydration level in thin films of the
Mater. Chem. A 3 (2015) 22824. biopigment eumelanin, J. Mater. Chem. C 4 (2016) 9544.
[25] J. Lv, Q. Zhou, T. Zhi, D. Gao, C. Wang, Environmentally friendly surface [43] B. Sun, S. Zhu, S. Mao, P. Zheng, Y. Xia, F. Yang, M. Lei, Y. Zhao, From dead leaves
modification of polyethylene terephthalate (PET) fabric by low-temperature to sustainable organic resistive switching memory, J. Colloid Interface Sci. 513
oxygen plasma and carboxymethyl chitosan, J. Clea. Prod. 118 (2016) 187. (2018) 774.
[26] W. Zhang, C. Wang, G. Liu, X. Zhu, X. Chen, L. Pan, H. Tan, W. Xue, Z. Ji, J. Wang, [44] Z. Xu, Z. Liu, Y. Huang, G. Zheng, Q. Chen, H. Zhou, To probe the performance of
Y. Chen, R.-W. Li, Thermally-stable resistive switching with a large ON/OFF perovskite memory devices: defects property and hysteresis, J. Mater. Chem. C
ratio achieved in poly(triphenylamine), Chem. Commun. 50 (2014) 11856. 5 (2017) 5810.