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1 r3) is pyroelectric, which implies it can be ferroelectric.
2 c, piezoelectric or pyroelectric response of ferroelectrics.
3 ics of many types of domain walls in various ferroelectrics.
4 ient energy harvesting devices using polymer ferroelectrics.
5 actions in uniaxial as opposed to multiaxial ferroelectrics.
6 stood 'waterfall' effect observed in relaxor ferroelectrics.
7 a crucial role in photovoltaic properties of ferroelectrics.
8 ly used to describe the structure of relaxor ferroelectrics.
9 structural effects on defect interactions in ferroelectrics.
10           We observed long range ordering of ferroelectric 109 degrees stripe nanodomains separated b
11 tric-field control has been demonstrated for ferroelectric 180 degrees domain walls, similar control
12 TiO3-BiZn0.5Ti0.5O3 (BT-BZT) polycrystalline ferroelectrics, a prototypical lead-free piezoelectric w
13 ectric toroidal order and a high-temperature ferroelectric a1/a2 phase.
14                     This long-range array of ferroelectric and ferroelastic domains can be useful for
15           Here, we report the observation of ferroelectric and ferroelastic nanodomains in (110)-orie
16 ultiferroics, in which (anti-)ferromagnetic, ferroelectric and ferroelastic order parameters coexist,
17 ifunctional materials contained simultaneous ferroelectric and ferromagnetic ordering have been reali
18 can be synthesized by integrating monolithic ferroelectric and magnetic materials, with interfacial c
19 ctric multiferroic because it maintains both ferroelectric and magnetic ordering to well above room t
20 realised by the hybridization of graphene, a ferroelectric and meta-atoms/meta-molecules, and extend
21                    Polarization switching in ferroelectric and multiferroic materials underpins a bro
22 strate the coexistence of antiferroelectric, ferroelectric and new ordered and low-symmetry phases.
23 lp understand the strong competition between ferroelectric and paraelectric phases as well as the pro
24 surface, and that spinoidal decomposition of ferroelectric and paraelectric phases occurs in non-stoi
25 ss a wide range of temperatures, in both the ferroelectric and paraelectric phases.
26                      However, the control of ferroelectric and phase switching and its correlation wi
27         The crystalline growth and the local ferroelectric and piezoelectric properties were evaluate
28  This work suggests a material with combined ferroelectric and semiconducting features could be a pro
29 n improving large polarizations in ultrathin ferroelectrics and are meaningful for the development of
30  new insight into the domain-wall physics in ferroelectrics and foreshadow the possibility to design
31 ated with historical data from literature on ferroelectrics, and expanded to functional materials for
32  are critical in determining the response of ferroelectrics, and the ability to controllably create,
33 n, rendering it ineffective for conventional ferroelectric applications and polarization switching.
34                                        While ferroelectrics are birefringent and non-linear optically
35                     Among such ferromagnetic ferroelectrics are conical spin spiral magnets with a si
36 in and enhance the polarization in nanoscale ferroelectrics are of scientific and technological impor
37 or decades due to the fact that vacancies in ferroelectrics are often charged and polarization in cha
38 rise to a polarization comparable to that of ferroelectric ATiO3.
39      While polarization inherently exists in ferroelectric barium titanate (BaTiO3), its high permitt
40 efficient way in developing highly efficient ferroelectric-based solar cells and novel optoelectronic
41 eld induced structural phase transition in a ferroelectric BaTiO3 nanoparticle.
42 ved in zero magnetic field using strain from ferroelectric BaTiO3 substrates to control perpendicular
43 0.3MnO3 electrodes separated by an ultrathin ferroelectric BaTiO3 tunnel barrier, where a head-to-hea
44                    By simply adding the nano-ferroelectrics (BaTiO3 nanoparticles) into the cathode,
45                                           As ferroelectrics become thinner, maintaining a stable pola
46 on acceptor and donor molecules that exhibit ferroelectric behavior along two distinct crystallograph
47 ature of the cocrystals, required to observe ferroelectric behavior, is demonstrated using second har
48                   All samples showed typical ferroelectric behavior.
49 prototypical example is PbTe whose incipient ferroelectric behaviour has been recently associated wit
50 erization that probes the full extent of the ferroelectric behaviour.
51 ), retains the polar space group of 1 and is ferroelectric below 260 K.
52 ies due to the formation of a self-polarized ferroelectric beta-phase and the creation of an electret
53  be mysteriously abundant in hybrid improper ferroelectric (Ca,Sr)3Ti2O7 crystals.
54 e BaTiO3 nanoparticle in a composite polymer/ferroelectric capacitor to study the behavior of a three
55                                              Ferroelectrics carry a switchable spontaneous electric p
56                           Flexible lead-free ferroelectric ceramic nanowire arrays exhibit a unique c
57  (PZT 52/48) and PbZr0.95Ti0.05O3 (PZT 95/5) ferroelectric ceramics under identical loading condition
58  as high as 1% in the voltage range near the ferroelectric coercive field.
59 nganese(II), an organic-inorganic perovskite ferroelectric crystal processed from aqueous solution, h
60 hombohedral Pb(Mg1/3Nb2/3)0.7Ti0.3O3(PMN-PT) ferroelectric crystal.
61 ielectric/piezoelectric responses of relaxor-ferroelectric crystals using a combination of cryogenic
62 nd conductivity through symmetry lowering in ferroelectric crystals.
63 rged conducting domain walls in the improper-ferroelectric Cu3B7O13Cl.
64 (diol) exhibit significant dielectric and/or ferroelectric dependence on different diol molecules.
65 ly 10(5) ) ever reported in room-temperature ferroelectric devices, opening new avenues for engineeri
66 n nanostructures is needed for miniaturizing ferroelectric devices.
67 capacitance in a model system of multidomain ferroelectric-dielectric superlattices across a wide ran
68 c material, we prepare a van der Waals (vdW) ferroelectric diode formed by CIPS/Si heterostructure, w
69                              The behavior of ferroelectric domain under applied electric field is ver
70                                              Ferroelectric domain walls are of great interest as elem
71                                              Ferroelectric domain walls constitute a completely new c
72                                              Ferroelectric domain walls have continued to attract wid
73                                              Ferroelectric domain walls hold great promise as functio
74 field control of the electronic transport at ferroelectric domain walls.
75 -proven fractional dimensionality of 2.5 for ferroelectric domain walls.
76 with local strains generated by a network of ferroelectric domain walls.
77 the developing of nanoscale devices based on ferroelectric domain walls.
78            Polymer thin films with patterned ferroelectric domains are attractive for a broad range o
79 their crystalline growth with highly ordered ferroelectric domains arrangements and, consequently, gr
80 grees domains walls; while for KNNLa/NSTO100 ferroelectric domains grow with the polarization pointin
81 e charges are naturally formed on unscreened ferroelectric domains in ambient condition.
82 m the collected surface charges on the poled ferroelectric domains in the P(VDF-TrFE) thin films.
83 mains, can be described by ferromagnetic and ferroelectric domains only.
84 insights into the formation and evolution of ferroelectric domains when the sample is ferroelectric d
85  formation of large polarons, Rashba effect, ferroelectric domains, and photon recycling.
86 t by the net polarization of the surrounding ferroelectric domains, such that it possesses a multi-or
87                                In this work, ferroelectric domains, surface termination, average latt
88       Observation of a new type of nanoscale ferroelectric domains, termed as "bubble domains"-latera
89 rmed due to competing interactions involving ferroelectric domains.
90 cale inhomogeneity, that coexist with normal ferroelectric domains.
91 i-step ferroelectric switching with multiple ferroelectric domains.
92                              Nanometer-scale ferroelectric dots and tubes have received a great deal
93  of ferroelectric domains when the sample is ferroelectric during the growth process.
94  suggest a facile method to discriminate the ferroelectric effect from the electromechanical (EM) res
95 n be used as a new tool to differentiate the ferroelectric effect from the other factors that contrib
96 polysulfide entrapping strategy based on the ferroelectric effect has been demonstrated for the first
97 k Schottky barriers, which are formed at the ferroelectric-electrode interfaces and blocking most of
98          Structure-property relationships in ferroelectrics extend over several length scales from th
99 ions of SrRuO3 /BaTiO3 /SrRuO3 (SRO/BTO/SRO) ferroelectric (FE) capacitors.
100 oping multifunctional materials, spin-driven ferroelectrics featuring both spontaneous magnetization
101 ittle fatigue by realization of a reversible ferroelectric-ferroelectric phase transition in [011] cu
102 ice distortions and/or octahedral rotations, ferroelectric-ferromagnetic interfaces are affected by s
103                                              Ferroelectrics (FEs) are materials of paramount importan
104 and capacitance tunable by external stimuli (ferroelectric field and magnetic field).
105 loited to realize a giant enhancement of the ferroelectric field effect in a prototype Mott field-eff
106                        Here we report a true ferroelectric field effect-carrier density modulation in
107 performance comparable to existing thin-film ferroelectric field-effect transistors.
108 ly enhances the pyroelectric response of the ferroelectric film under near-infrared irradiation.
109 rally deteriorated or even vanishes when the ferroelectric films are downsized to unit cell scale.
110 e also demonstrate the use of such patterned ferroelectric films for near-infrared sensing/imaging.
111 spontaneous polarization in ultrathin BiFeO3 ferroelectric films is reported.
112 e report dielectric ultracapacitors based on ferroelectric films of Ba(Zr0.2,Ti0.8)O3 which display h
113  the role of strain-polarization coupling in ferroelectric films with nontrivial anharmonicities and
114                    Examples include improved ferroelectrics for memory devices and materials that hos
115 modulation of photoluminescence tuned by the ferroelectric gating, potentially finding applications i
116 lear how the underlying structure of relaxor ferroelectrics gives rise to their defining properties,
117 ization is usually coupled to strain, making ferroelectrics good piezoelectrics.
118 wo-dimensional steep-slope transistor with a ferroelectric hafnium zirconium oxide layer in the gate
119 derlying piezoelectric properties of relaxor ferroelectrics has yet to be established.
120  made in this subject especially on magnetic/ferroelectric heterostructures.
121 Finally, PBI-OVDF and Pc-OVDF materials show ferroelectric hysteresis behavior together with high rem
122 chers have demonstrated that BiFeO3 exhibits ferroelectric hysteresis but none have shown a strong fe
123 ally leaky materials as MAPbI3, we show here ferroelectric hysteresis from well-characterized single
124       This excludes normal measurements of a ferroelectric hysteresis loop, to prove ferroelectricity
125 vial texture for the square) and, hence, non-ferroelectric, in contrast to previous predictions from
126   While neither perovskite AVO3 nor AFeO3 is ferroelectric, in the double perovskite A 2VFeO6 a 'comp
127 states near the band edges that leads to the ferroelectric instability in PbTe.
128 -induced polarization reversal and strain in ferroelectrics is an ongoing challenge that so far has o
129 nt of electronic properties in complex-oxide ferroelectrics is demonstrated whereby ion bombardment -
130 ty of spontaneous electrical polarization in ferroelectrics is fundamental to many of their current a
131 cluding normal-, relaxor-, organic- and anti-ferroelectrics is imperative for exploiting new flexible
132 The tunability of electrical polarization in ferroelectrics is instrumental to their applications in
133                 Formation of domain walls in ferroelectrics is not energetically favourable in low-di
134 ced conductivity at specific domain walls in ferroelectrics is now an established phenomenon.
135           The next step, proving it is (not) ferroelectric, is challenging, because of the material's
136 layer with spontaneous polarization into the ferroelectric ITO/PZT/Au film, a p-n junction with stron
137    More importantly, the introduction of the ferroelectric layer induces the memory window without dr
138 ty for resonator with an arbitrary number of ferroelectric layers is formulated.
139 Finally, the possible application of the two ferroelectric layers structures for switchable microwave
140 ical inputs, with each connected to separate ferroelectric layers that act as the multi-level control
141 ross the interface due to strain-rejuvenated ferroelectric-like instabilities in the materials.
142 3 substrate is accompanied with head-to-head ferroelectric-like polarizations across the interface du
143                                          The ferroelectric-like polarizations and electron-hole juxta
144 owever, one remaining issue of ferromagnetic/ferroelectric magnetoelectric bilayer composite is that
145 eculiar features of domain walls observed in ferroelectrics make them promising active elements for n
146  and hysteretic dielectric polarization from ferroelectric material in vacuum (P 10(-6) torr).
147 fication with dielectric polarization from a ferroelectric material in vacuum to dramatically enhance
148                    Single-crystal perovskite ferroelectric material is integrated at room temperature
149 h orthogonal polarization directions) in the ferroelectric material PbTiO3 to provide microscopic ins
150      To demonstrate the potential of this 2D ferroelectric material, we prepare a van der Waals (vdW)
151 ing the sizes of devices, the preparation of ferroelectric materials and devices is entering the nano
152 r control of the bulk photovoltaic effect in ferroelectric materials by nanoscale engineering of thei
153             The device potential of these 2D ferroelectric materials is further demonstrated using th
154 in-film, solution-processable supramolecular ferroelectric materials is rare.
155 arization and inversion symmetry breaking in ferroelectric materials lead to their use as photovoltai
156                                              Ferroelectric materials possess spontaneous polarization
157 ates the potential of preparing a new set of ferroelectric materials simply by attaching OVDF oligome
158 ly, the advantageous functional responses in ferroelectric materials that make them attractive for us
159 s (FMBC) utilizing the ability of multiaxial ferroelectric materials to pin the polarization at a seq
160       By unravelling the correlation between ferroelectric materials' responses to solar irradiation
161 ent suggests that, despite the complexity of ferroelectric materials, typical ferroelectric switching
162 steresis loop that is a signature feature of ferroelectric materials.
163  predicting and optimizing the properties of ferroelectric materials.
164  fuels devices can be enhanced by the use of ferroelectric materials.
165 l structure on the macroscopic properties of ferroelectric materials.
166 olution single crystals is a breakthrough in ferroelectric materials.
167 d, which makes them unstable and uncommon in ferroelectric materials.
168 c, pyroelectric and electronic properties of ferroelectric materials.
169 cs, where the polar nanoregions aligned in a ferroelectric matrix can facilitate polarization rotatio
170 he macroscopic polarization of a surrounding ferroelectric matrix-is reported.
171  film thickness, allowing the realization of ferroelectric memories with device dimensions far below
172 rical read-out of the polarization states in ferroelectric memories.
173                                 The existing ferroelectric memory cells are based on the two-level st
174 dy the multiferroic domains in ferromagnetic ferroelectric Mn2GeO4 using neutron diffraction, and sho
175                              Here we propose ferroelectric multibit cells (FMBC) utilizing the abilit
176     A controllable ferroelastic switching in ferroelectric/multiferroic oxides is highly desirable du
177 9.0 microC cm(-2) are successfully probed in ferroelectric nanocapacitors and thin films, respectivel
178 axation of the spontaneous polarization in a ferroelectric nanocrystal.
179 icity to the finite lateral-size effect of a ferroelectric nanodot with an additional effect possibly
180 l model, our simulations show that arrays of ferroelectric nanosynapses can autonomously learn to rec
181                  We note that the material's ferroelectric nature, can, but need not be important in
182                                     Adding a ferroelectric negative capacitor to the gate stack of a
183  phthalocyanines (Pc) bearing three to eight ferroelectric oligomers at their periphery.
184  in thin film samples induced by traditional ferroelectric or flexible substrates is usually volatile
185 ic or acousto-optic effect in single-crystal ferroelectric or polar compounds such as LiNbO3 or quart
186                                Moreover, the ferroelectric order couples to the ferrimagnetism, enabl
187 order parameters coupled to ferroelastic and ferroelectric order in multiferroic materials.
188 familiar dipolar terms responsible for (anti)ferroelectric order.
189  years, tremendous progress has been made in ferroelectric oxide thin film technology-a field which i
190 hysical properties of prototypical ABO3 bulk ferroelectric oxides.
191 NCs) as plasmonic nanostructures to induce a ferroelectric-paraelectric phase transition in a poly(vi
192 erroic system consisting of a (011)-oriented ferroelectric Pb(Mg,Nb,Ti)O3 substrate intimately couple
193     By switching the polarization field of a ferroelectric Pb(Zr,Ti)O3 (PZT) gate, nonvolatile resist
194 nsisting of ultrathin ferromagnetic NiFe and ferroelectric Pb0.92La0.08Zr0.52Ti0.48O3 (PLZT) films, w
195                                    Recently, ferroelectric perovskite oxides have drawn much attentio
196                                              Ferroelectric perovskite oxides such as BaTiO3 and PbTiO
197 ransition from the paraelectric phase to the ferroelectric phase at this temperature, which causes th
198 ing rapidly as one transitions away from the ferroelectric phase transition (TC).
199                   The compound experiences a ferroelectric phase transition ascribed to the 6s(2) lon
200  an incipient ferroelectric with an expected ferroelectric phase transition extrapolated to lie at 6
201 tion of the soft modes underlying successive ferroelectric phase transitions.
202 ween two variants of the stable low-symmetry ferroelectric phase.
203 f this reversible transformation between two ferroelectric phases and advance towards the development
204 s interconversion between the vortex and the ferroelectric phases concomitant with order-of-magnitude
205  room temperature, the coexisting vortex and ferroelectric phases form a mesoscale, fibre-textured hi
206 in and polar lattice modes can stabilize new ferroelectric phases from nonpolar dielectrics or enhanc
207 in, we develop a new approach to enhance the ferroelectric photovoltaic effect by introducing the pol
208  However, the power conversion efficiency of ferroelectric photovoltaic effect currently reported is
209 etimes may make this system interesting as a ferroelectric photovoltaic.
210                                              Ferroelectric polarization and domains should then evolv
211 to investigate the influence of vacancies on ferroelectric polarization and polarization switching in
212 r practical applications, simultaneous large ferroelectric polarization and strong magnetoelectric co
213   Vacancies play a pivotal role in affecting ferroelectric polarization and switching properties, and
214 eneral formulae Cu1-xIn1+x/3P2S6, have shown ferroelectric polarization behavior with a T c above the
215 rlying Ge(001) substrate by switching of the ferroelectric polarization in epitaxial c-axis-oriented
216 orce microscopy, we studied the evolution of ferroelectric polarization in response to external and b
217 tion and hole transportation on the basis of ferroelectric polarization in TiO2 -SrTiO3 core-shell na
218                      The magnetic control of ferroelectric polarization is currently a central topic
219 Fe(3+) -O-Co(3+) bonds, while the suppressed ferroelectric polarization is due to the enhanced leakag
220 ble nature of the single-domain out-of-plane ferroelectric polarization of BaTiO3 is confirmed using
221 ered-perovskite Bi2WO6 thin films, where the ferroelectric polarization rotates by 90 degrees within
222 uch as the magnetic-field-driven reversal of ferroelectric polarization with no change of spin-helici
223 ar single crystals has been shown to exhibit ferroelectric polarization, demonstration of stimuli-res
224 apacitance depends on the orientation of the ferroelectric polarization.
225  two classes of shift current photovoltaics, ferroelectric polymer films and single-layer orthorhombi
226                  Up until now, however, only ferroelectric polymers have intrinsically met this flexi
227 present a comprehensive review of the use of ferroelectric polymers, especially PVDF and PVDF-based c
228 ory of quantum criticality for such uniaxial ferroelectrics predicts that the temperature dependence
229 report the structure evolution, magnetic and ferroelectric properties in Co-doped 4- and 3-layered in
230                           Precise control of ferroelectric properties through composition, size and c
231 aterials, which exhibit coupled magnetic and ferroelectric properties, have attracted tremendous rese
232 age and deposition time on the structure and ferroelectric property of the P(VDF-TrFE) films was stud
233 ion hysteresis loop clearly demonstrates the ferroelectric property.
234 e allows us to generate patterned domains of ferroelectric PVDF within just a few seconds.
235 d perpendicular anisotropy grown directly on ferroelectric PZT [Pb(Zr0.52Ti0.48)O3] substrate plates.
236                                     However, ferroelectric reliability issues, such as imprint, reten
237                   In this study, everlasting ferroelectric retention in the heteroepitaxially constra
238 field simulations, the key to the success of ferroelectric retention is to prevent the crystal from f
239 ng a new approach to overcome the failure of ferroelectric retention.
240                        Research on nanoscale ferroelectrics reveals that their behaviour is profoundl
241 re-dependent dielectric anomalies as well as ferroelectric reversible spontaneous polarization.
242 l PbZr0.2 Ti0.8 O3 /SrTiO3 /PbZr0.2 Ti0.8 O3 ferroelectric sandwich structures due to the interplay b
243 dynamics; whereas Smax in relaxor and normal ferroelectrics scales as Smax V cr(-0.37), which talli
244 0.95Zr0.05TiO3, Pb0.8Ba0.2ZrO3 and polymeric ferroelectrics scales proportionally with V cr(-2.2), ow
245 universal property of topological defects in ferroelectric semiconductors.
246 te recognition events into dielectric and/or ferroelectric signals.
247  phase modulation of THz beam by operating a ferroelectric single crystal LiNbO3 film device at the p
248 Pb(Mg1/3Nb2/3)O3-PbTiO3 (PIN-PMN-PT) relaxor ferroelectric single crystal.
249 ary Pb(In1/2Nb1/2)O3-Pb(Mg1/3Nb2/3)O3-PbTiO3 ferroelectric single crystals have potential application
250                                      Relaxor ferroelectric single crystals have triggered revolution
251 )-oriented domain-engineered ternary relaxor ferroelectric single crystals with extended temperature
252     Sr3 Sn2 O7 is the first room-temperature ferroelectric Sn insulator with switchable electric pola
253 e has not been experimentally verified to be ferroelectric so far.
254 ttering analyses to an important non-relaxor ferroelectric solid solution exhibiting the so-called co
255 ery of ultrahigh piezoelectricity in relaxor-ferroelectric solid solution single crystals is a breakt
256                   A key signature of relaxor-ferroelectric solid solutions is the existence of polar
257 The electric susceptibility of the incipient ferroelectric SrFe12O19, which is slightly further from
258  its intrinsically high charge mobility, the ferroelectric SrTiO3 thin shell significantly improves t
259  ferrimagnetic LuFe2O4 into a simultaneously ferroelectric state, while also reducing the LuFe2O4 spi
260 tization switching in a hybrid ferromagnetic/ferroelectric structure with Pt/Co/Ni/Co/Pt layers on PM
261 ss of polar topologies possible in ultrathin ferroelectric structures and bring forward the prospect
262 itation of acoustic eigenmodes in multilayer ferroelectric structures is considered, and the principl
263 pendicular magnetic anisotropy combined with ferroelectric substrates represent a new approach toward
264  attention, triggered notably by low-bandgap ferroelectrics suitable for sunlight spectrum absorption
265 ibly coming from the existence of a thin non-ferroelectric surface layer.
266                                              Ferroelectric susceptibilities are, in general, strongly
267  work, the phases, dielectric properties and ferroelectric switching behavior of strontium lead titan
268 mplexity of ferroelectric materials, typical ferroelectric switching is largely governed by a simple,
269                               Here we report ferroelectric switching of ferromagnetic resonance in mu
270                                          The ferroelectric switching of magnetic anisotropy exhibits
271  we develop an approach for rapid probing of ferroelectric switching using direct strain detection of
272 orts utilized approaches based on multi-step ferroelectric switching with multiple ferroelectric doma
273  currents by 5 orders of magnitude, improved ferroelectric switching, and unprecedented insights into
274                      In epitaxially strained ferroelectric thin films and superlattices, the ferroele
275 asable conductive domain walls in insulating ferroelectric thin films can be used for non-destructive
276       Controlled switching of resistivity in ferroelectric thin films is demonstrated by writing and
277 strated by interfacing 2D semiconductors and ferroelectric thin films, exhibiting superior memory per
278 size effect of 180 degrees stripe domains in ferroelectric thin films, there have been numerous repor
279 devices, opening new avenues for engineering ferroelectric thin-film devices.
280 use the effective electric permittivity of a ferroelectric to become negative, enabling it to behave
281 roelectric thin films and superlattices, the ferroelectric transition temperature can lie above the g
282                                          The ferroelectric transition temperature T(c) of 1-UC SnTe f
283          Here we report on synapses based on ferroelectric tunnel junctions and show that STDP can be
284 e show that in unpoled Co/PbTiO3/(La,Sr)MnO3 ferroelectric tunnel junctions, the polarization in acti
285 ovskite has been found, theoretically, to be ferroelectric under epitaxial strain becoming a promisin
286    We demonstrate the synthesis of metallic, ferroelectric, upconversion, semiconducting, and thermoe
287 nnihilation centres of pairs of two types of ferroelectric walls (and also Z3-vortex pairs) in 90 deg
288     Charged polar interfaces such as charged ferroelectric walls or heterostructured interfaces of Zn
289                                      Charged ferroelectric walls, which are energetically unfavourabl
290 igin of the high piezoelectricity in relaxor ferroelectrics, where the polar nanoregions aligned in a
291  a possibility if MAPbI3 is a semiconducting ferroelectric, which, however, requires clear experiment
292 ur is profoundly different from that in bulk ferroelectrics, which could lead to new phenomena with p
293                     Different from a typical ferroelectric whose electric polarization is easily satu
294 ly, we find that the layered oxides are also ferroelectric with a spontaneous polarization approachin
295                           It is an incipient ferroelectric with an expected ferroelectric phase trans
296 Starting with hexagonal LuFeO3-the geometric ferroelectric with the greatest known planar rumpling-we
297 001) films of layered A3B2O7 hybrid-improper ferroelectrics with experimentally accessible biaxial st
298  requirement, leaving small-molecule organic ferroelectrics with room for improvement.
299 e external stimuli for domain engineering in ferroelectrics with significant current leakage.
300 z - 2)/z, where the dynamical exponent for a ferroelectric z = 1 and the dimension is increased by 1

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