ライフサイエンスコーパス: tensile

1 CNTs led to an increase in the compressive, tensile and bond strengths of specimens compared to thos

2 The compressive, tensile and bond strengths of the samples with and witho

3 model for the mycelium which reproduces the tensile and compressive behavior of the material.

4 The resulting nanoscale alternating tensile and compressive strain fields lead to considerab

5 S's ability to dynamically track microscopic tensile and compressive strains across diverse biologica

6 ectrical conductivity within a wide range of tensile and compressive strains.

7 The tensile and flexural moduli improved with the addition o

8 t and dispersity (D) are known to affect the tensile and rheological properties of HDPE, but little i

9 Here we manipulate tensile and shear mechanical stress in the bacterial cel

10 to current single-modulus models, decoupling tensile and shear responses.

11 dhesively bonded joints are subject to mixed tensile and shear stresses when the restoration is in oc

12 ornea, obtaining values consistent with both tensile and shear tests.

13 of the rotaxane provokes the accumulation of tensile and torsional stress that ultimately leads to th

14 nterpret various physical forces like shear, tensile, and compression stress.

15 lls are constantly subjected to compressive, tensile, and shear forces, which regulate nucleoskeletal

16 provide record performance as torsional and tensile artificial muscles, they are expensive, and only

17 It is shown that the tensile behavior of the rostrum across six Curculio spec

18 rformed by means of atomic force microscopy, tensile biaxial deformation, and real-time deformability

19 statistic, and separate Mann-Whitney tests, tensile bond strengths to wet- and dry-bonded dentin ind

20 We found that tensile cell stress leads to rapid ACKR2 down-regulation

21 Tensile characteristics were determined between temporal

22 Both Driselase and Cel12A increased the tensile compliance, but differently for elastic and plas

23 the indentation compliance without changing tensile compliances.

24 nsition from creep to strain recovery fits a tensile-compressive linear viscoelastic model that is in

25 ed carbon nanotube yarn muscles that provide tensile contraction as high as 16.5%, which is 12.7 time

26 do not require a liquid electrolyte, provide tensile contractions of 11.6% and 5%, respectively.

27 ental evolution of the elastic strain during tensile deformation at 973 K.

28 Unidirectional step-cycle tensile deformation has been applied to these polyamides

29 Under constant amplitude cyclic tensile deformation, RBCs progressively lose their abili

30 lloy chemistry, friction stir processing and tensile deformation.

31 -centered cubic (bcc) beta-titanium alloy on tensile deformation.

32 nce in friction stir processed, annealed and tensile-deformed specimens.

33 e southern Wasatch Fault at c. 0.5 mm yr(-1) tensile dislocation opening in the eastern Sevier Desert

34 a in as-printed and post-processed forms and tensile ductilities of greater than 13% at room temperat

35 ile yield stress (~900 MPa) with appreciable tensile ductility (>20%), via annealing at 700 degrees C

36 ture (~450 MPa) concurrent with high uniform tensile ductility (~35%).

37 t ensures that flow is delocalized, enhances tensile ductility and inhibits catastrophic mechanical f

38 n-hardening capability that promotes uniform tensile ductility.

39 th without compromising strain hardening and tensile ductility.

40 ultimate tensile strength (UTS) via uniaxial tensile elongation analysis (~75 MPa).

41 both as a likely site of crack initiation in tensile failure and as a source of morphological constra

42 ent flexibility, stretchability, outstanding tensile fatigue resistance (over 50,000 times) and under

43 eased carbon fibre content, the quasi-static tensile/flexural stiffness and strength increases follow

44 Inhibiting TRPV4 decreased tensile force across vinculin, whereas TRPV4 activation

45 that IGPR-1 is activated by shear stress and tensile force and that flow shear stress-mediated IGPR-1

46 icient for activation or whether exertion of tensile force by the actin cytoskeleton across the integ

47 n of integrin adhesiveness by application of tensile force by the cytoskeleton, across ligand-integri

48 es the rate of oxidative addition, whereas a tensile force decreases the rate, relative to that of th

49 molecules which actin-cytoskeleton-generated tensile force takes when applied through the integrin be

50 The cytokinetic ring generates tensile force that drives cell division, but how tension

51 n was imaged at the same time as an external tensile force was applied to live vascular smooth muscle

52 ntegrin activation, where the development of tensile force yields physiological integrin activation.

53 imes that initially increase with increasing tensile force.

54 tive cytoskeletal networks under an external tensile force.

55 In this report, using tensile-force assays, immunofluorescence and atomic forc

56 low-driven shear stress (FFCM) increased the tensile forces and increased migratory potential.

57 r ablation supports the conclusion that that tensile forces are stored across the apical surface of e

58 uct membrane DNA tension probes to visualize tensile forces at cell junctions.

59 r spindle integrity in mitotic cells so that tensile forces generated at kinetochores do not cause mi

60 tretch-growth, suggesting a possible role of tensile forces in MT translocation/assembly.

61 teocyte-conditioned media (CM) decreased the tensile forces in their focal adhesions and decreased th

62 Local compressive and tensile forces on the order of 100 pN were generated usi

63 istribution, and orientation of the opposing tensile forces remain poorly characterized.

64 f epithelial cells, and anillin promotes the tensile forces stored in this network.

65 ular adhesive landscape, revealing ring-like tensile forces surrounding podosome cores.

66 probes that measure and manipulate podosome tensile forces with molecular piconewton (pN) resolution

67 can be broadly used to measure intercellular tensile forces.

68 stic response of T2DM RBCs subject to static tensile forcing and their viscoelastic relaxation respon

69 hod and preliminary data that simulates both tensile fracture and fluid flow at elevated pressures.

70 rehole to move through the freshly generated tensile fracture to a voluometer.

71 ighly conductive flow paths can be formed in tensile fractures by creating corrugated surfaces.

72 lylactic acid, enabling the fabrication of a tensile gauge functioning via the readjustment of the el

73 Omega/Omega%, which compares well with other tensile gauges.

74 The TC was maximised for strong tensile in-plane strain which produced weak octahedral r

75 nitude less than those (few MPa) obtained by tensile/inflation testing.

76 er quasi-static (strain-rate = 10(-3) s(-1)) tensile loading and dynamic (strain-rate = 10(3) s(-1))

77 enhanced single fiber composites (SFC) under tensile loading to understand the interfacial improvemen

78 ar origin of strain hardening using uniaxial tensile loading, microspectroscopy of polymer chain alig

79 have been tested under monothonic and cyclic tensile loads up to ultimate failure.

80 ble to withstand substantial compressive and tensile loads, and exhibit a remarkable self-healing eff

81 ds is an order of magnitude lower than under tensile loads.

82 tions, motorized excised larynx experiments, tensile material tests and high-speed imaging, we show t

83 contraction of alpha' imposed an interphase tensile microstress in the transverse direction of the g

84 With tensile moduli of approximately 9.1 MPa, ultimate tensil

85 d region- and strain-dependent variations in tensile moduli, associated with regional differences in

86 tes [Formula: see text] 2.5% s(-1), both the tensile modulus and strength of the BC nanopapers stayed

87 ng from 350 to 1100 nm and substrates with a tensile modulus of approximately 4-8 MPa.

88 e triaxial fibers contributing to the higher tensile modulus.

89 work capacity by factors of 1.70 to 2.15 for tensile muscles driven electrothermally or by vapor abso

90 -banding in bulk samples in normal uniaxial (tensile or compressive) tests, prevents catastrophic fai

91 rn harvesters that electrochemically convert tensile or torsional mechanical energy into electrical e

92 Then, we have applied hydrostatic tensile pressure at two different expansion rates in the

93 on bubble should continue to grow as long as tensile pressure continues to increase in the system.

94 in the chamber induces localized compressive/tensile pressure cycles, with an amplitude that is consi

95 synthesis agents, leads to neocartilage with tensile properties approaching those of native tissue.

96 r of theoretical and experimental studies on tensile properties of carbon nanotubes (CNT), reporting

97 The obtained materials display the tensile properties of commercial polyolefins but adhere

98 However, the tensile properties of engineered tissues have remained f

99 chnique, we will be able to directly measure tensile properties of millimeter-long MWCNTs.

100 ates of 25% s(-1) and 50% s(-1) however, the tensile properties of the BC nanopapers decreased signif

101 We analysed tensile properties of the fishing lines of the New Zeala

102 ffness was increased grossly, but changes in tensile properties were not statistically significant.

103 s commercial iPP while demonstrating similar tensile properties.

104 anisotropic human neocartilage with enhanced tensile properties.

105 e the in-plane polarization dominates at the tensile regions.

106 A serrated tensile response corresponding to stress oscillations wa

107 nfluences of grammage and strain rate on the tensile response of bacterial cellulose (BC) nanopaper.

108 This observed anomalous tensile response of BC nanopaper is attributed to inerti

109 typical failure mode can be generalized as "tensile-rupture and sheared-sliding" (TRSS).

110 at decrease P311 levels could result in less tensile scars, which could potentially lead to higher in

111 econd approach is to manufacture small-scale tensile specimens containing only the proton irradiated

112 Initially, tensile specimens of a Co-added stainless steel were hea

113 Tensile specimens were subsequently loaded at 350 degree

114 to substantiate a generalized model for the tensile stiffness of hierarchical filamentous networks w

115 cellulose microfibrils influenced creep and tensile stiffness whereas homogalacturonan influenced in

116 Tensile storage modulus and heat flow measurements were

117 Further, we have reported that 10% cyclic tensile strain (1 Hz, 4 hours/day) enhances hASC osteoge

118 a diameter of 60 nm exhibit highest elastic tensile strain (13.4%) and tensile strength (125 GPa).

119 chondrocytes (BACs) were subjected to cyclic tensile strain (CTS) loading.

120 rvix (CAM) and examined the effect of cyclic tensile strain (CTS) on mediators involved in mechanotra

121 man mesenchymal stem cells (hMSCs) to cyclic tensile strain (CTS).

122 ng electrode, that enabled us to resolve how tensile strain affects hydrogen absorption and HER activ

123 y cilia exhibit mechanosensitivity to cyclic tensile strain and lineage-dependent expression, which m

124 oving the mechanochromic sensitivity to both tensile strain and normal force (critical tensile strain

125 Here we report maximum achievable tensile strain and strength of diamond nanoneedles with

126 improvements in HER and OER activities with tensile strain are due to an increase in concentration o

127 s a germanium nanowire under a 1.6% uniaxial tensile strain as the gain medium.

128 Further, we show that cyclic tensile strain both enhances osteogenic differentiation

129 Mechanical deformations up to 50% tensile strain do not induce significant loss of the ele

130 y lower than predicted value due to a larger tensile strain effect on the a-axis compared to the comp

131 Ni(2+) ion is under-bonded by a significant tensile strain from neighboring Ag(2) Se(2) layers, lead

132 thesize that primary cilia respond to cyclic tensile strain in a lineage dependent manner and that th

133 We stabilized uniform extreme tensile strain in nanoscale La(0.7)Ca(0.3)MnO(3) membran

134 It is proposed that accumulated transient tensile strain in the excitation region plays a crucial

135 nd Raman spectroscopy reveals a 3.8% biaxial tensile strain in the germanium nanostructures.

136 trong reduction of ionic conductivity, while tensile strain increases the unit-cell volume while quen

137 In this study, a uniaxial tensile strain is applied to thin flakes of the vdW magn

138 ft in the OER overpotential is observed when tensile strain is applied to TiO(2).

139 Tensile strain is known to improve the electrocatalytic

140 y, found that monatomic steps and Au-induced tensile strain on PtIr facilitate C-C bond splitting via

141 ent magnitude, signalling a benign effect of tensile strain on the carrier transport properties of Mo

142 ambiguous fingerprint of dynamically-induced tensile strain that reaches values up to ~4 x 10(-4) und

143 a custom electrochemical cell, which applies tensile strain to a flexible working electrode, that ena

144 amplitude, and orientation as a function of tensile strain to resolve the crack-free structural tran

145 n survive 1000 stretch-release cycles of 20% tensile strain with small fluctuations in electrolumines

146 roelectricity in SrTiO(3) with 2.0% uniaxial tensile strain, corroborated by the notable features of

147 Tc the CI phase is further stabilized under tensile strain, for X = Pd and Pt a site disproportionat

148 Driven by tensile strain, GaAs quantum dots (QDs) self-assemble on

149 rodes were subjected to mechanically-applied tensile strain, the amount of hydrogen that absorbed int

150 At 3% tensile strain, the HER overpotential required to genera

151 tent Ge(0.94)Sn(0.06) layers by implementing tensile strain.

152 ous metal catalysts when the TiO(2) is under tensile strain.

153 mpressive strain, while the a-plane exhibits tensile strain.

154 ffect, i.e. the conductivity decreases under tensile strain.

155 ffect from the extrinsic contributions under tensile strain.

156 nt of T( *) in SmB6 under the application of tensile strain.

157 th tensile strain and normal force (critical tensile strain: 50% and normal force: 1 N).

158 show the advantages of using low Sn content tensile strained GeSn layers in respect to gain and lasi

159 umber of exsolved particles as compared with tensile-strained films.

160 ing from piezoresponse force spectroscopy of tensile-strained PbZr(0.2)Ti(0.8)O(3) with a hierarchica

161 h increasing GaAs deposition, even after the tensile-strained QDs (TSQDs) have begun to form.

162 In this study, we show that the tensile-strained self-assembly process for these GaAs(11

163 modification in resistivity is observed for tensile-strained SmNiO(3), substantially different from

164 including those generated on the fly during tensile straining, also offer elevated strain-hardening

165 Large in-plane compressive and out-of-plane tensile strains (-3.6% and +4.9%, respectively) were ind

166 le moduli of approximately 9.1 MPa, ultimate tensile strains of approximately 325%, compressive stren

167 Uniquely, BNNT/PDMS accommodates tensile strains up to 60% without plastic deformation by

168 dles can sustain exceptionally large elastic tensile strains with high tensile strengths, the size- a

169 served domains of increasing compressive and tensile strains.

170 t highest elastic tensile strain (13.4%) and tensile strength (125 GPa).

171 These GO/Mfp films display high tensile strength (134-158 MPa), stretchability (~ 26% el

172 Improved tensile strength (73 +/- 11 MPa) in machine produced str

173 rial cellulose macrofibers yield record high tensile strength (826 MPa) and Young's modulus (65.7 GPa

174 Highest tensile strength (87 +/- 21 MPa) was recorded for CS str

175 elongation (from 3.18 to 13.59%), decreased tensile strength (from 22.71 to 3.97 MPa), increased wat

176 ed that Er:YAG + HF had significantly higher tensile strength (p = 0.00).

177 strength (sigma y) of 1260 MPa, and ultimate tensile strength (sigma UTS) of 1400 MPa.

178 We present estimates of ultimate tensile strength (UTS) for two engineered beta-solenoid

179 ulus (EM), maximum strain (MS), and ultimate tensile strength (UTS) in the 20-Gy group were significa

180 und to possess the same approximate ultimate tensile strength (UTS) via uniaxial tensile elongation a

181 lf-heal at room temperature with a recovered tensile strength 4 MPa, which is 30% of its original val

182 ts in Zn-0.8Li-0.4Mg alloy with the ultimate tensile strength 646.69 +/- 12.79 MPa and Zn-0.8Li-0.8Mn

183 abricated a new scaffold exhibiting (1) high tensile strength and biomechanical properties comparable

184 tion of the essential oil increased ultimate tensile strength and contact angle but decreased elongat

185 The acetylation decreased the tensile strength and increased the elongation of the fil

186 d biomechanical properties by increasing its tensile strength and load.

187 had increased stiffness, providing a higher tensile strength and lower elongation when compared to f

188 aling elastomers at room temperature, with a tensile strength and toughness up to 14.8 MPa and 87.0 M

189 ysical properties of materials, such as high tensile strength and toughness, but also improved proces

190 interfacial fracture properties, such as the tensile strength and work of separation, using atomistic

191 The tensile strength and Young's modulus at MPa levels are c

192 ic scaffolds relying solely on high uniaxial tensile strength are poor with high rates of implant rup

193 anisms in one material, leading to twice the tensile strength compared to a single-phase HEA with sim

194 ressing lines supported a role for ZmCtl1 in tensile strength enhancement.

195 tion with AFM showed significantly increased tensile strength for Fg interacting with the E652D/H782Q

196 usceptibility, but moreover show exceptional tensile strength in both as-welded and post-weld heat-tr

197 5-fold (transverse direction) lower ultimate tensile strength in comparison with Hastalex (p < 0.05).

198 0 mum and widths exceeding 50 mm and biaxial tensile strength in excess of 3 MPa, were produced by pu

199 antly accelerated closure time and increased tensile strength in mice, and was validated in the porci

200 verned by the interfibrillar matrix, whereas tensile strength is dominated by collagen fibrils.

201 Our material has a tensile strength of 1,300 megapascals and 10 per cent el

202 created micro-sized pyrolytic carbon with a tensile strength of 1.60 +/- 0.55 GPa, a compressive str

203 t room temperature with an instant recovered tensile strength of 1.84 MPa and a continuously increase

204 As a result, an ultra-high tensile strength of 2.4-2.6 GPa, a significant elongatio

205 grees C) and superior mechanical properties (tensile strength of 250 MPa) are achieved due to the int

206 excellent mechanical properties with a high tensile strength of 342 MPa and a Young's modulus of 43.

207 The fibre exhibits a tensile strength of 895 MPa and a stretchability of 44.3

208 d mechanical robustness (a high longitudinal tensile strength of 91.95 MPa and toughness of 2.73 MJ m

209 rmolecular cross-links are essential for the tensile strength of collagen fibrils.

210 In the presence of RE, the tensile strength of film decreased, whereas the extract

211 ty of 2.58 mWh g(-1) or 3.6 mWh cm(-3), high tensile strength of over 1000 MPa, and bearable pressure

212 Tensile strength of the biofilm infected skin was compro

213 s the modulus (or stiffness), toughness, and tensile strength of the fibers.

214 When normalized by weight, the specific tensile strength of the macrofiber is as high as 598 MPa

215 cyclic stress amplitudes much lower than the tensile strength of the materials involved.

216 eriments at stress amplitudes lower than the tensile strength of the metal, we report a history-indep

217 retains the native protein conformation and tensile strength of the natural ACL but is decellularize

218 not affect the water vapor permeability and tensile strength of the OSA-based carrier.

219 ure in the intrusion overcomes the effective tensile strength of the particle pack, a localised chann

220 ligned cellulose nanofibers has a mechanical tensile strength of up to 350 MPa, nearly three times of

221 strain value than dried threads, whereas the tensile strength of wet threads was much lower.

222 bulk structural material with a record high tensile strength of ~1 GPa and toughness of 9.74 MJ m(-3

223 The loss of amniotic epithelial cells and tensile strength preceding membrane rupture is poorly un

224 econd-order models were fitted to the SD and tensile strength responses; while the cubic model demons

225 these polyamides and significantly enhances tensile strength to over 210 MPa while maintaining elast

226 These films demonstrate record tensile strength up to ~570 MPa for a 940 nm thick film

227 The ultimate tensile strength was 1165 MPa with ductility of ~18% and

228 ratio of crosslinking functional groups, the tensile strength was controlled, ranging from 0.14+/-0.0

229 example, chemical and thermal resistance and tensile strength) comes at the expense of degradability

230 into the wound environment, increased wound tensile strength, and a higher ratio of type I:type III

231 impart the resulting nanocomposite a higher tensile strength, and elastic and storage moduli.

232 entrations of FJP and CG reduced the maximum tensile strength, and increased CG increased the elongat

233 orders of magnitude increases in stiffness, tensile strength, and tensile toughness compared to its

234 ucture and concentration on elastic modulus, tensile strength, and ultimate strain.

235 anofiber diameter of 502 +/- 150 nm, and the tensile strength, contact angle, porosity, water vapor p

236 structure contribute to its high mechanical tensile strength, flexural strength, and toughness.

237 ictates the bulk material properties such as tensile strength, modulus, and glass transition.

238 mpressive properties such as remarkable unit tensile strength, modulus, and resistance to heat, flame

239 other properties such as ultimate toughness, tensile strength, poroviscoelastic responses, energy dis

240 ile testing results showed that the ultimate tensile strength, the elongation at failure, and the ten

241 Mechanical properties of the fiber such as tensile strength, young's modulus have also been investi

242 hift of yield strength, strain hardening and tensile strength.

243 ckness is strongly correlated with increased tensile strength.

244 y, dermal thickness, collagen deposition and tensile strength.

245 lus, yield strength, and especially ultimate tensile strength.

246 ent increment of the elastic modulus and the tensile strength.

247 with reduced stiffness but also reduced scar tensile strength.

248 me and increased mucus strand elasticity and tensile strength.

249 s by 24.8% (P < 0.0001) without compromising tensile strength.

250 heir abilities to form networks of different tensile strengths and to encapsulate, protect and releas

251 ally large elastic tensile strains with high tensile strengths, the size- and orientation-dependence

252 scores, error scores, leak volumes, and knot tensile strengths.

253 embranes demonstrated higher antifouling and tensile stress (by 31%) when compared to pure PES membra

254 modeling revealed significant reductions in tensile stress and elastic-plastic deformation during di

255 Membrane deformation upon swelling generates tensile stress and internal pressure, contributing to vo

256 As a second step, we calculated the tensile stress experienced by the cell wall along the fi

257 ubule alignment along growth-derived maximal tensile stress in adjacent cells would mechanically isol

258 and incrementally increasing (i.e. dynamic) tensile stress is an effective tool for dynamically tuni

259 roles in stiffening the cell wall where the tensile stress is high and exposes cells to bursting, an

260 The maximum tensile stress of the optimal hybrid construct was 3.42

261 Thermal tensile stress perpendicular to the laser scanning direc

262 Tensile stress relaxation is combined with transmission

263 In this model, we considered the maximum tensile stress tangential to the interfacial surface, as

264 y deform the nucleus by applying a transient tensile stress to the nuclear membrane.

265 ear deformation and the magnitude of applied tensile stress.

266 nds and to challenge their stability against tensile stress.

267 s the nuclear membranes against rupture from tensile stress.

268 min A,C, and histone deacetylation, as these tensile stresses 1) are transmitted to the nucleus throu

269 cell geometric constraints affect the local tensile stresses and subsequently the three-way feedback

270 clear deformations typically caused by local tensile stresses are sufficient to cause nuclear membran

271 Local tensile stresses can also cause nuclear deformations, bu

272 t notably in plant cells where turgor-driven tensile stresses exceed greatly those observed in animal

273 ous adhesion failure estimation under cyclic tensile stresses from a resistivity baseline.

274 The model shows local tensile stresses generated at the interface of the cell

275 reduction in significant levels of residual tensile stresses in the graphite that are 'frozen-in' fo

276 the Piezo1 channel as a key TM transducer of tensile stretch, shear flow and pressure.

277 e interactions between surface atoms lead to tensile surface stresses that exert a pressure on the or

278 of this alloy increases with the increasing tensile temperature.

279 tropic plasticity by picking an axisymmetric tensile test rig, in which shear localization is rarely

280 Dynamic rheology measurements of the DFP and tensile testing of the resulting fibers reveal design co

281 Furthermore, micro-tensile testing results showed that the ultimate tensile

282 However, tensile testing reveals that the MWD skew does not impac

283 A carefully designed tensile testing technique for the MWCNTs is developed, w

284 Tensile testing was performed, but results were not stat

285 is hypothesis was supported by the result of tensile testing, which showed that the MD membrane was s

286 al computed tomography (AS-OCT) imaging, and tensile testing.

287 id syndrome and was analyzed with AS-OCT and tensile testing.

288 without light-activation of RAFT during the tensile testing.

289 to the stress-strain curves obtained in the tensile tests and statistically compared.

290 Tensile tests indicated that UFG-1 steel had high yield

291 Quasi-static uniaxial tensile tests were performed in nasal-temporal direction

292 ny other macroscale carbon films; microscale tensile tests yield maximum values of 290 GPa for the Yo

293 Macroscale tensile tests yields maximum values of 62 GPa for the Yo

294 ral changes during nanoindentation and micro-tensile tests, indicating that the core region possessed

295 ncreases in stiffness, tensile strength, and tensile toughness compared to its iron-free precursor wh

296 strength, the elongation at failure, and the tensile toughness of single fibers could be significantl

297 performing unconfined compression, splitting tensile, triaxial, and direct shear tests.

298 of plane stress in this layer is found to be tensile, which acts as the driving force for the crack g

299 ovel nano-lamellar microstructure exhibits a tensile yield strength of 1074 MPa with a reasonable duc

300 rant FCC + B2 microstructure, retaining high tensile yield stress (~900 MPa) with appreciable tensile