ライフサイエンスコーパス: polycrystalline

1 lms for solar cells, are either amorphous or polycrystalline.

2 NMR spectra show that the Fe(CO)3 moiety in polycrystalline 4c (but not 4a) undergoes rapid rotation

3 on process can aid in rational design of the polycrystalline absorber films, leading to their enhance

4 nted thin films, and for CO and HCOO(-) over polycrystalline Ag and Sn.

5 nm amorphous-phase Co nanocrystals and 4 nm polycrystalline Ag nanocrystals at 25 degrees C, triangl

6 thod to unravel microstructural evolution of polycrystalline Al microstructures at the mesoscales.

7 Our findings have shown that for polycrystalline alumina ceramics, an average grain size

8 ic circuitry and ultra-broadband imaging but polycrystalline and amorphous thin films have shown infe

9 made with scalable fabrication techniques is polycrystalline and contains inherent nanoscale line and

10 The gradient FeNi nanowires exhibit polycrystalline and crystal twinning at different areas

11 The optical gap energies of both polycrystalline and epitaxial ITO thin films decrease wi

12 erior perovskite morphology and its inherent polycrystalline and highly defective nature.

13 enomenon in GBs with different structures in polycrystalline and nanocrystalline materials, where the

14 y of materials have been synthesized in both polycrystalline and single crystal form, and their struc

15 hotogenerated via singlet exciton fission in polycrystalline and single-crystalline pentacene is repo

16 ies to suppress charge recombination in both polycrystalline and single-crystalline perovskite solar

17 l CO2 reduction catalysis mediated by planar polycrystalline Au surfaces.

18 concerted proton-electron transfer (CPET) to polycrystalline Au was probed indirectly by studying the

19 The achieved ZT is nearly 50% higher than polycrystalline averaged single crystal ZT of ~0.4, and

20 stribution and chemomechanical properties of polycrystalline battery materials.

21 properties for enhancing the performance of polycrystalline battery materials.

22 rate, followed by overgrowth of high quality polycrystalline BDD (pBDD) and polishing to reveal appro

23 regions of sp(2) carbon into a high quality polycrystalline BDD electrode.

24 Thermoelastic deformation mechanisms in polycrystalline biomedical-grade superelastic NiTi are s

25 Past studies of polycrystalline BPs were challenged by the existence of

26 icroplates, thin films, single crystals, and polycrystalline bulks), and advanced device design (ther

27 Polycrystalline Ca3-xTbxCo4O9 (x = 0.0-0.7) samples were

28 ation of enhanced thermoelectric response in polycrystalline Ca3Co4O9 on doping Tb ions in the materi

29 two industrially important binary tellurides-polycrystalline cadmium and bismuth tellurides- were stu

30 of tubule-delineating cells, and consist of polycrystalline calcium phosphate similar to the mineral

31 The laser-sculptured polycrystalline carbides (macroporous, ~10-20 nm wall th

32 Growth of polycrystalline CdMnTe ternary compound thin films has b

33 tomography, carrier lifetimes are mapped in polycrystalline CdTe photovoltaic devices.

34 Recent experiments in polycrystalline, centrosymmetric perovskites (for exampl

35 tals, whereas the dielectric spectrum of the polycrystalline ceramic changes very little on poling.

36 rmed that the (In + Nb) co-doped rutile TiO2 polycrystalline ceramic had semiconductor grains and ins

37 red in the [001] and [111] directions with a polycrystalline ceramic of the same composition.

38 ctric behavior and impedance spectrum of the polycrystalline ceramic sample indicated that the intern

39 ved in a lead-free (Bi1/2 Na1/2 )TiO3 -based polycrystalline ceramic.

40 [111] cut crystal, and is not present in the polycrystalline ceramic.

41 e that the high translucency and strength of polycrystalline ceramics can be achieved through microst

42 Nb) co-doped rutile TiO2 single crystal and polycrystalline ceramics.

43 iented specimen relative to the conventional polycrystalline ceramics.

44 ation of single-crystal calcite (CaCO3) into polycrystalline cerussite (PbCO3) through reaction with

45 mately 220 nm in 2 ns for solution-processed polycrystalline CH3NH3PbI3 thin films.

46 nd Na(+) at pH 6 formed dendritic growth and polycrystalline circular assemblies on air-water interfa

47 in superdense nonmagnetic cobalt layers in a polycrystalline cobalt thin film.

48 an organic matrix that arrange in fibre-like polycrystalline configurations.

49 Blue-phase specimens, however, are generally polycrystalline, consisting of randomly oriented domains

50 arbon monoxide reduction reaction (eCORR) on polycrystalline copper and elucidated the oxygen incorpo

51 f hydrocarbons (-1 V vs RHE), even on smooth polycrystalline copper electrodes.

52 of these catalysts often being comparable to polycrystalline copper foil.

53 ut the electrochemical reduction of CO2 over polycrystalline copper.

54 formation from single-crystalline Co(4) N to polycrystalline CoS(x) that are rich in active sites.

55 ial to address the challenges present in its polycrystalline counterpart by reducing phase boundaries

56 s, current) over 3,000 times higher than its polycrystalline counterpart under moderate overpotential

57 transport and enhanced stability over their polycrystalline counterparts, due to their orientation-d

58 viding greater capacity retention than their polycrystalline counterparts.

59 s an example, we use high-quality single and polycrystalline crystals, various probes, including elec

60 ural evolution of the near-surface region of polycrystalline Cu electrodes under in situ conditions t

61 from the terraces and stepped sites found on polycrystalline Cu foil.

62 ntire commercially available decimeter-sized polycrystalline Cu foils are successfully transformed in

63 ) surface can be readily achieved on stacked polycrystalline Cu foils via simple oxygen chemisorption

64 a preferential surface reconstruction of the polycrystalline Cu surface toward (100) facets in the pr

65 Polycrystalline Cu surfaces were gradually oxidized in O

66 ately 200 to approximately 17,000 MOmega(-1) Polycrystalline CuI thin films were deposited at room te

67 Polycrystalline CuRhO2 is investigated as a photocathode

68 l diode), compared with a value of 3.1 for a polycrystalline deposit.

69 we introduce a direct approach to transform polycrystalline diamond into high-quality graphene layer

70 s ranging from 0.7 to 10 MPa) on 4 different polycrystalline diamond substrates with topography chara

71 Cantilevers based on polycrystalline diamond surfaces are very promising as c

72 ated for chemically grafting porcine OBPs on polycrystalline diamond surfaces for biosensor developme

73 lucidate the mechanism of graphene growth on polycrystalline diamond.

74 Polycrystalline diradical 2 forms a novel one-dimensiona

75 nd is amenable to sintering into monolithic, polycrystalline discs at 200 degrees C and about 300 MPa

76 The long-range order is disrupted by polycrystalline disorder and the variations in electrost

77 nometres, and the realization so far of only polycrystalline DNA-interconnected nanoparticle superlat

78 ew characterization method for understanding polycrystalline domain structure and transport in plasti

79 films grown by vapour deposition tend to be polycrystalline due to the nucleation and growth of isla

80 ted CO reduction on Cu(100), Cu(111), and Cu(polycrystalline) electrodes in 0.1 M alkaline hydroxide

81 Using Li3OCl as a model polycrystalline electrolyte, we apply large-scale molecu

82 and hence they can affect the performance of polycrystalline engineering alloys.

83 oscillations in linear birefringence of many polycrystalline ensembles is accompanied by oscillations

84 t 2,600~3,000 degrees C and exhibits a micro-polycrystalline feature.

85 ielectric, and specific heat measurements on polycrystalline FeCr2S4 in external magnetic fields.

86 n size effects on the physical properties of polycrystalline ferroelectrics have been extensively stu

87 onstrated for BaTiO3-BiZn0.5Ti0.5O3 (BT-BZT) polycrystalline ferroelectrics, a prototypical lead-free

88 tals (e.g., in gamma and X-ray detectors) to polycrystalline films (e.g., in photovoltaics, photodete

89 Here, we demonstrate that polycrystalline films of chemically identical molecules

90 We report on SF in thin polycrystalline films of two terrylene-3,4:11,12-bis(dic

91 ities of all depths of the interfaces of the polycrystalline films were one to two orders of magnitud

92 substrates by different deposition methods, polycrystalline films with excess Ge were frequently obt

93 In fact, in the case of polycrystalline films, depending on the synthetic route,

94 Although this process yields highly polycrystalline films, the optical constants are in agre

95 ering chloride-capped CdTe nanocrystals into polycrystalline films, where Cl selectively segregates i

96 manner the proton-withdrawing conditions of polycrystalline films, where excess basic precursors are

97 up to 8 x 10(-4) cm/(V s) were obtained for polycrystalline films.

98 exchange bias phenomenon is not possible in polycrystalline films.

99 an exceptionally useful nanomaterial in its polycrystalline form with applications in catalysis, ene

100 In polycrystalline form, Ca3Co4O9 is known to exhibit much

101 s with auxetic homogenous Poisson's ratio in polycrystalline form.

102 om a disordered amorphous form to an ordered polycrystalline form.

103 2-ylidene (Ir-NHC-Me2) complex adsorbed on a polycrystalline gold electrode.

104 liquid crystals (LCs) supported on ultrathin polycrystalline gold films (predominant crystallographic

105 Using a polycrystalline gold thin film subjected to heating, we

106 e is known about the mechanical roles of the polycrystalline grains that constitute the ferritic matr

107 r dynamics simulations of nanoindentation on polycrystalline graphene at different sites including gr

108 Consequently, the failure behavior of polycrystalline graphene by nanoindentation is criticall

109 simulations to study the failure behavior of polycrystalline graphene by varying both grain size and

110 We show that polycrystalline graphene fails in a brittle mode and gra

111 Here, graphene flakes, nucleated over a polycrystalline graphene film, synchronize during growth

112 layer-by-layer assembly of 100 single-layer polycrystalline graphene films is reported.

113 hene biosensors reported so far are based on polycrystalline graphene flakes which are anchored on su

114 Polycrystalline graphene is characterized using advanced

115 the grain size-dependent failure behavior of polycrystalline graphene is important for its applicatio

116 the first statistical theory of toughness in polycrystalline graphene, and elucidate the nanoscale or

117 f research reported in the past few years on polycrystalline graphene.

118 rmal, mechanical and optical properties of a polycrystalline graphene.

119 ons of grain boundaries, and applications of polycrystalline graphene.

120 by shock compression of pyrolytic as well as polycrystalline graphite to pressures from 19 GPa up to

121 nd starting at 50 GPa for both pyrolytic and polycrystalline graphite, we also record the direct form

122 bed by defects, leading to a rich variety of polycrystalline growth forms.

123 ced face-centered cubic titanium (fcc-Ti) in polycrystalline hexagonal close packed titanium (hcp-Ti)

124 monstrate that the superconductivity in bulk polycrystalline hexagonal epsilon-NbN is below approxima

125 rt the new discovery of superconductivity in polycrystalline hexagonal epsilon-NbN synthesized at hig

126 incompressibility and high shear rigidity of polycrystalline hexagonal epsilon-NbN using ultrasonic i

127 have been many promising candidates (such as polycrystalline HgI(2) and CdTe), none of the semiconduc

128 Bulk polycrystalline high-entropy carbides are a newly develo

129 to a flexible fiber-like substrate, which is polycrystalline, highly flexible, ultralong, and mechani

130 te a new and low-cost method for fabricating polycrystalline III-nitrides, which have a range of inte

131 s) are comparable to reference devices using polycrystalline indium tin oxide (ITO) electrodes.

132 ition at approximately 3.2 K was observed in polycrystalline ingots.

133 Herein, polycrystalline InN, GaN and systematically controlled I

134 and shear moduli (K and G, respectively) for polycrystalline inorganic compounds, using 1,940 compoun

135 interfacial regions show a thin region with polycrystalline Ir nanocrystals.

136 more complete Li-storage occurring in porous polycrystalline iron fluoride, and further, incomplete c

137 k-etched polymers to synthesize (i) vertical polycrystalline La0.7Sr0.3MnO3 nanorods on top of single

138 acitance may result from LIG's unusual ultra-polycrystalline lattice of pentagon-heptagon structures.

139 Light scattering by the polycrystalline lenses is minimized by the use of relati

140 0(5) are fabricated by depositing a layer of polycrystalline lithium niobate on the flat top surfaces

141 on the fabrication of such solar cells from polycrystalline, low purity (99.98%) p-type silicon star

142 tes remain obscured by extensive disorder in polycrystalline MAPbX3 films.

143 dynamics of ubiquitin to be even more like a polycrystalline material in which the alpha-helix and be

144 Polycrystalline material properties depend on the distri

145 These results pave the way for understanding polycrystalline material response under external stimuli

146 Grain boundaries create strained regions in polycrystalline materials by stabilizing dislocations an

147 The physical properties of polycrystalline materials depend on their microstructure

148 e plastic deformation when the grain size of polycrystalline materials goes small.

149 Recent investigations in thin film polycrystalline materials have shown the formation of co

150 ly activated mobility previously observed in polycrystalline materials is caused by grain boundary re

151 Polycrystalline materials synthesized by an iodine-catal

152 oundly important determinant of character in polycrystalline materials that is not well understood.

153 als changes in the local atomic structure in polycrystalline materials under fields.

154 Although many approaches focus on polycrystalline materials(5-7), single-crystal hybrid pe

155 ce in the deformation of nanocrystalline and polycrystalline materials, but comprehensive understandi

156 urity or phonon-impurity scattering in these polycrystalline materials, which supports high charge-ca

157 le junctions are a key structural element in polycrystalline materials.

158 l length scales for both single crystals and polycrystalline materials.

159 ated to damage and deformation mechanisms in polycrystalline materials.

160 s general implications for the properties of polycrystalline materials.

161 erature deformation and recrystallization of polycrystalline materials.

162 dislocation activity leads to brittleness of polycrystalline materials.

163 n be incorporated in situ during growth of a polycrystalline membrane of the MOF ZIF-8.

164 The pure-phase Zr-MOF (i.e., UiO-66) polycrystalline membranes were fabricated on alumina hol

165 gested that the thermoelectric properties of polycrystalline metal nanowires are related to grain str

166 Polycrystalline metal oxides find diverse applications i

167 organic semiconductor molecule, polymer, and polycrystalline metal, respectively.

168 plication of dipole engineering to versatile polycrystalline metal/binary oxide functional interfaces

169 esented results demonstrate the potential of polycrystalline metals for antiferromagnetic spintronics

170 mpositionally heterogeneous surfaces such as polycrystalline metals, and ensemble-type electrodes exe

171 e temperature ductility minimum" observed in polycrystalline metals.

172 Here we turn to polycrystalline methylammonium lead iodide perovskite, w

173 f growth of tension and compression twins in polycrystalline Mg microstructures at high strain rates.

174 r stress-relieved but recrystallizing into a polycrystalline microstructure, paving the way for addit

175 sub-grain scale stress gradients present in polycrystalline microstructures, which often lead to fat

176 e report the preparation of highly textured, polycrystalline Mn3Ge films on amorphous substrates, wit

177 n form factor is investigated in single- and polycrystalline-MnNiGa samples using small-angle neutron

178 Thin films of highly textured ZnO and polycrystalline Mo serve as semiconductors for light gen

179 Using our results, we propose a polycrystalline model to quantify the impact of grain bo

180 aterials properties as well as supporting 3D polycrystalline modelling of materials performance.

181 thod to investigate the photoconductivity of polycrystalline MOF samples as-prepared.

182 yrmion bubbles in perpendicularly magnetised polycrystalline multilayers patterned into 1 microm diam

183 Co-doped MoS(2-x) polycrystalline nanosheets with S vacancies as the catal

184 e development of photoelectrode design in 1D polycrystalline nanotube arrays, 1D single-crystalline n

185 Results from the XRD indicated the polycrystalline nature of the electrodeposited films.

186 Owing to the high chemical purity and polycrystalline nature, the MoS(2) nanostructures demons

187 the formation of an alpha-MoO3 phase with a polycrystalline nature.

188 PL was performed in both single-crystal and polycrystalline NGO (substrates and pellets) respectivel

189 rature is discovered, where a porous, rough, polycrystalline NH4 PbI3 non-perovskite thin film conver

190 upled Ni-deficient Li(x)NiO nanoclusters and polycrystalline Ni nanocrystals and its exceptional acti

191 In bismuth-doped polycrystalline nickel, we found that ordered, segregati

192 al plasticity simulation, was conducted on a polycrystalline nickel-based superalloy microstructure n

193 nowires with approximately 17 mum length and polycrystalline NiO(x) membrane are observed by both fie

194 and dissolution (e.g., crevice corrosion) of polycrystalline nonnoble metals, alloys, and inorganic m

195 ve to the orientation of grain boundaries in polycrystalline OIPCs.

196 nsor to have superior uniformity compared to polycrystalline ones.

197 space and 3D reciprocal space for almost any polycrystalline or multi-phase material.

198 emperature under uniaxial stress can convert polycrystalline or single-crystal benzene monomer into s

199 By exposing a polycrystalline organic material, consisting of a XB-acc

200 d crystallization can yield solution-printed polycrystalline organic semiconductor films with transpo

201 ing on charge transport in the most relevant polycrystalline organic semiconductors is reviewed, and

202 n lengths greater than 100 nanometers in the polycrystalline organolead trihalide compound CH3NH3PbI3

203 n oxides are only applicable to amorphous or polycrystalline oxide nanosheets or films.

204 ualitatively distinct from commonly observed polycrystalline packings contradicts conventional wisdom

205 ortance of interior local environment within polycrystalline particles for electrochemical reactions

206 hydrothermal approach is used to synthesize polycrystalline particles with sizes ranging from <200 n

207 ace-to-bulk" charge distribution prevails in polycrystalline particles, the crystallographic orientat

208 with the interior local environments within polycrystalline particles.

209 antified from over 20 million nanodomains in polycrystalline particles.

210 y charge separation from triplet excitons in polycrystalline pentacene using an electrochemical serie

211 However, the mobility and trap densities of polycrystalline perovskite films are still significantly

212 efforts on preparing uniform and large-grain polycrystalline perovskite films have led to enhanced ca

213 fect of large morphological heterogeneity of polycrystalline perovskite films on their device perform

214 sulting in a preferred growth orientation of polycrystalline perovskite films with reduced trap state

215 and diffusivities, in neat CH3 NH3 PbI3 (Cl) polycrystalline perovskite films, the local (intra-grain

216 Manipulation of grain boundaries in polycrystalline perovskite is an essential consideration

217 arrays that are distinguishable from general polycrystalline perovskite materials in terms of their c

218 vapor-assisted solution process to construct polycrystalline perovskite thin films with full surface

219 des (PeLEDs) based on three-dimensional (3D) polycrystalline perovskites suffer from ion migration, w

220 se transition at ~ 200 degrees C and develop polycrystalline phases with increased optical gap energi

221 ear response under strong light, superior to polycrystalline photodetectors.

222 ivity and stability of Ni3S2 exceeds that of polycrystalline platinum and manganese, nickel, and coba

223 entally measured hydrogen binding energy for polycrystalline platinum examined in several buffer solu

224 mm-sized, single-crystal graphene by coating polycrystalline platinum foils with a silicon-containing

225 techniques to study hydrazine oxidation on a polycrystalline platinum substrate both in air and in a

226 Hypochlorite oxidation on polycrystalline platinum yields ClO. radicals, which ini

227 cifically the electro-oxidation of iodide at polycrystalline platinum-reveals unique (i.e., structure

228 COF-701 is obtained as a polycrystalline powder and possesses permanent microporo

229 7, which was synthesized in the form of bulk polycrystalline powder via high-temperature solid-state

230 1 are characterized by SQUID magnetometry of polycrystalline powders, in polystyrene glass, and in ot

231 Using polycrystalline Pt as a model system, correlative SECCM

232 smooth surface mainly composed of thin-film polycrystalline Pt, with some apparent nanoscale roughne

233 The materials are among the most active polycrystalline Pt-based catalysts reported, presenting

234 e demonstrate current-induced switching in a polycrystalline PtMn/Pt metallic heterostructure.

235 single crystal pyrite and nanocrystalline or polycrystalline pyrite films for successful solar applic

236 ield applied to a chiral liquid crystal with polycrystalline quasi-hexagonal arrangements of self-ass

237 le with field and laboratory observations of polycrystalline rocks), coupled to an idealized model of

238 A polycrystalline sample of 1 displays three sextets in th

239 the highest value observed till date in any polycrystalline sample of this system.

240 Indentation testing on a well-sintered polycrystalline sample yielded the hardness of 11.8(4) G

241 rved low-field magnetoresistance effect in a polycrystalline sample.

242 (1+y)(Zn,Mn)P is obtained in Li(1+y)(Cd,Mn)P polycrystalline samples by Arrott plot technique.

243 Although previous studies on polycrystalline samples have identified a 105-K phase tr

244 the possibility of efficient DNP transfer in polycrystalline samples of [Co(en)3Cl3]2.NaCl.6H2O (en =

245 re dependence of the SCO phase transition in polycrystalline samples of protonated and partially deut

246 terizing the mechanical behavior of tungsten polycrystalline samples with ion-irradiated surfaces.

247 solutions can exhibit higher zT compared to polycrystalline samples.

248 2-delta)(As(1-x)P(x))(2) (delta ~ 0.07-0.22) polycrystalline samples.

249 In polycrystalline semiconductors, grain boundaries are oft

250 ostic and applicable to other disordered and polycrystalline semiconductors.

251 The presence of the Ni layer as a polycrystalline shell completely hindered the light emis

252 iven core-shell morphology that emerges when polycrystalline shells of ZIF-8 (zeolitic imidazolate fr

253 probe the real-time interfacial dynamics of polycrystalline Si particles growing from an Al-Si-Cu li

254 d on the character of the twin boundaries in polycrystalline Si photovoltaic cells.

255 raphitic domains ( approximately 2.5 nm) and polycrystalline silicon ( approximately 5 nm).

256 While usually based on either amorphous or polycrystalline silicon (alpha-Si and poly-Si, respectiv

257 Here, we demonstrate wavelength-scale polycrystalline silicon (pSi) PhC microresonators with Q

258 eliability issues of a-Si:H, low-temperature polycrystalline silicon and amorphous oxide semiconducto

259 diagnosis of bladder cancer, using an n-type polycrystalline silicon nanowire field-effect transistor

260 wn the operating temperature of a commercial polycrystalline silicon solar cell by 17 degrees C under

261 t room temperature; however, the traditional polycrystalline silver electrocatalyst requires a large

262 Measurements of polycrystalline silver films over a range of distances (

263 g time, it has not been directly observed on polycrystalline silver films which suffer from significa

264 approximately 20 times higher) compared with polycrystalline silver.

265 e and interparticle electrostatic repulsion, polycrystalline, single-crystalline and quasi-amorphous

266 However, nanocrystalline or polycrystalline SnSe offers a wide range of thermoelectr

267 tal halide perovskite single-crystalline and polycrystalline solar cells.

268 ermolecular quintet at room temperature as a polycrystalline solid is studied.

269 e, orientation, and defects of inhomogeneous polycrystalline solids by raster scanning them under a m

270 Much like energy transport in polycrystalline solids, hydraulic transport in semi-orde

271 anic materials that exhibit this behavior as polycrystalline solids.

272 The protocol is applied to polycrystalline specimens of two different dipeptide nan

273 it from high-density "random-close packing" polycrystalline states and hence provides a stringent te

274 Magnetization measurements show that polycrystalline superconducting (SC) K(1.9)Fe(4.2)Se(5)

275 Studies using single crystals suggest a polycrystalline surface should display an inhomogeneous

276 y for industrial applications, are typically polycrystalline - that is, composed of single-crystallin

277 it is essential to develop high-performance polycrystalline thermoelectric materials.

278 ological evolution of a chemically deposited polycrystalline thin film.

279 e manipulated, here, we investigate SB-CS in polycrystalline thin films of 1,6,7,12-tetra(phenoxy)per

280 Singlet fission (SF) in polycrystalline thin films of four 3,6-bis(thiophen-2-yl

281 roscopic approaches, Wenger et al. show that polycrystalline thin films possess similar optoelectroni

282 ld an efficiency enhancement 44-fold that of polycrystalline thin films, due to the much longer carri

283 erovskite photodetectors are mainly based on polycrystalline thin films, which have some undesired pr

284 of TSCs are 10-100 folds lower than that of polycrystalline thin films.

285 ely studied in two forms: single-crystals or polycrystalline thin films.

286 le crystals are almost identical to those of polycrystalline thin films.

287 rap densities in the single crystals than in polycrystalline thin films.

288 he manufacturing process involves doping the polycrystalline thin-film CdTe with CdCl2.

289 Large-aspect-ratio grains are needed in polycrystalline thin-film solar cells for reduced charge

290 820 nm, 20 nm broader than the corresponding polycrystalline thin-film solar cells.

291 , with average value similar to results from polycrystalline thin-film studies.

292 All-perovskite-based polycrystalline thin-film tandem solar cells have the po

293 efficient two-terminal all-perovskite-based polycrystalline thin-film tandem solar cells.

294 best-performing, extrinsically doped p-type polycrystalline tin selenides.

295 ells over the ZnO NRs gradually changed from polycrystalline to single crystalline.

296 Lastly, defect structures in monolayer polycrystalline transition metal dichalcogenides grown b

297 Atomically thin polycrystalline transition-metal dichalcogenides (TMDs)

298 X-Ray diffraction confirmed the formation of polycrystalline tungsten oxide.

299 y contributes to the possible application of polycrystalline W under irradiation in advanced nuclear

300 We demonstrate that UV-light activation of polycrystalline ZnO films on flexible polyimide (Kapton)