ライフサイエンスコーパス: spinel

1 ation into a copper aluminate phase (CuAl2O4 spinel).

2 nominal charges of the atomic species in the spinel.

3 y of CoAl(2)O(4), a highly frustrated A-site spinel.

4 , attributed to iron oxide-bearing aluminous spinel.

5 cifically in the magnesium scandium selenide spinel.

6 or electrochemical performance of disordered spinel.

7 e origin of the markedly superior ability of spinel {111} facets, resulting from strong interactions

8 cation to CoO and to Fe(2)SiO(4) olivine and spinel, a quenched high pressure phase metastable at amb

9 yite), Mn3O4 (hausmannite), and lambda-MnO2 (spinel), all containing Mn(III) possessing longer Mn-O b

10 orated into the matrix of magnesio aluminate spinel-alumina (MA-A) via infiltration of a porous prefo

11 Spinel and diopside in the CAI cores are 16O-rich (Delta

12 the cubic close packed subarray of Fe(3)O(4) spinel and gamma-Fe(2)O(3).

13 e of topical materials encompassing layered, spinel and polyanionic framework compounds such as LiCoO

14 logical Clapeyron slopes of the (Mg,Fe)2SiO4 spinel and postspinel transformations.

15 or the cation ordering in LiNi(0.5)Mn(1.5)O4 spinels and correlate the stress patterns, phase evoluti

16 , with the brittle mode more dominant in the spinels and the quasi-plastic mode more dominant in the

17 ase in the lattice structure of high voltage spinel, and its effect on the charge transport propertie

18 tal structures, and test the formula against spinel- and olivine-group minerals that have well-constr

19 nanoparticles (AuNPs) supported on MgCuCr2O4-spinel are highly active and selective for the aerobic o

20 Experiments with doped spinels at 700 degrees C provide quantitative confirmati

21 ons of the relative stability of layered and spinel bulk phases of Co oxides, as well as the stabilit

22 on the cation sublattice that are present in spinel but not in pyrochlore.

23 rovides a framework by which the behavior of spinel can be more accurately modeled under the extreme

24 ed that the local structure of Mg1-xNixAl2O4 spinel cannot be understood as simply being due to catio

25 The Cu-Mn spinel catalyst is robust and reused three times under o

26 evaluate damage accumulation in alumina and spinel ceramics with different pre-form grain morphologi

27 hene oxide sheets and cation substitution of spinel Co(3)O(4) nanoparticles, a manganese-cobalt spine

28 of these results to those from a pure phase spinel Co3O4 catalyst supports this interpretation and r

29 of the Co(OH)2 and partial conversion of the spinel Co3O4 phases to CoO(OH) under precatalytic electr

30 diated growth, high-quality and monodisperse spinel cobalt ferrite, CoFe(2)O(4), nanocrystals can be

31 ity of LT-LiCoO2 is higher than that of both spinel cobalt oxide and layered lithium cobalt oxide syn

32 oxide nanoparticles supported on mesoporous spinel cobalt oxide, which catalyses the conversion of c

33 tion in the physical properties of different spinel compositions.

34 apacitance (in excess of 500%) for the cubic spinel compound CdCr2S4 and related isomorphs, concludin

35 pyrochlores, the amorphization resistance of spinel compounds correlates directly with the energy to

36 Here we show that a series of lacunar spinel compounds, GaM4X8 (M=Nb, Mo, Ta and W and X=S, Se

37 s the activity descriptor for the ORR/OER of spinels, consolidating the role of electron orbital fill

38 ypothesis that glass-infiltrated alumina and spinel core ceramics are resistant to damage accumulatio

39 origin of the unusual spin structure of the spinel CoV2O4, which stands at the crossover from insula

40 (III) and the formation of a Cr-incorporated spinel, Cr2O3, and Cr(OH)3 phases.

41 The spinel crystallographic structure, first solved by Bragg

42 xygen carrier can avoid the formation of the spinel CuAl(2)O(4) and significantly reduce carbon depos

43 anoclusters of the room-temperature magnetic spinel CuCr(2)S(4) have been synthesized using a facile

44 In the ferromagnetic spinel CuCr2Se4-xBrx, the resistivity rho (at low temper

45 At first sight, the quenched tetragonal spinel CuMn(2)O(4) can be formulated with Cu(2+) and Mn(

46 A magnetic transition in iron silicate spinel, detected previously by Mossbauer spectroscopy, i

47 ing atmosphere leads to the formation of the spinel Fe3O4 phase which displays a distinct ferrimagnet

48 elimination of APBs in other members of the spinel ferrite family, such as Fe3 O4 and CoFe2 O4 , whi

49 action indicated that, during oxidation, the spinel ferrite lattice remains intact while structural F

50 Magnetic cobalt spinel ferrite nanoparticles coated with biocompatible p

51 Spinel ferrite NiFe2 O4 thin films have been grown on th

52 ontrast, Cd(II) ions either did not form the spinel ferrite structure or were not incorporated into t

53 ion of technetium into a family of synthetic spinel ferrites that have environmentally durable natura

54 d of the divalent oxide and expansion of the spinel field appear to be general phenomena.

55 ough Mg substitution in the mesoporous Co3O4 spinel, followed by a Mg-selective leaching process.

56 The spinel from the white rind has an isotopic composition s

57 gallium oxohydroxide (GaOOH) and the defect spinel, gamma-gallium oxide (gamma-Ga(2)O(3)).

58 The lacunar spinel GaTa4Se8 was theoretically predicted to form the

59 and understanding the cation distribution in spinels has been one of the most interesting problems in

60 Tc(IV) incorporation in spinels has been proposed as a novel method to increase

61 ORR/OER activities of other transition-metal spinels, including Mnx Co3-x O4 (x = 2, 2.5, 3), Lix Mn2

62 Further evidence of a spinel inclusion is provided by analysis of the magnetic

63 8 eV (2.07 eV form XANES), consistent with a spinel inclusion.

64 The formation of stable spinel inclusions in a QD has not been previously report

65 ons leads to formation of small ZnCr(2)Se(4) spinel inclusions within the cubic sphalerite lattice of

66 inum/magnesium in circumstellar corundum and spinel is considered to reflect various stages of back-r

67 ent of the (electro)chemical behavior of the spinel is undertaken without forming a conductive compos

68 rporation of Tc(IV) has little effect on the spinel lattice structure.

69 s rarely coexist in geometrically-frustrated spinel lattices.

70 However, it converts to the defect spinel LiFe5O8 on cycling.

71 of H2O, thus converting LiFeO2 to the defect spinel LiFe5O8 on cycling.

72 ce morphology and composition giving rise to spinel-like and amorphous surface structures, respective

73 Nanocrystalline spinel LiMn(2)O(4) has been prepared and treatment of Li

74 attice mismatch between the involved phases, spinel LiMn1.5Ni0.5O4 is capable of fast rate even at la

75 , and Li2GeO3, Li4NiTeO6 and Li2MnO3 for the spinel LiMn2O4 cathodes.

76 ambda-MnO2, where the latter is derived from spinel LiMn2O4 following partial Li(+) removal.

77 TiO2 followed by post-annealing treatment on spinel LiNi0.5 Mn1.5 O4 (LNMO) cathode material is devel

78 Spinel LiNi0.5Mn1.5O4 is shown to have a uniform distrib

79 Zero-strain electrodes, such as spinel lithium titanate (Li4/3Ti5/3O4), are appealing fo

80 Spinels (M(3)O(4)) commonly have lower surface energies

81 intercalation/deintercalation of Li-ions in spinel materials enables not only energy storage but als

82 amond lattice, realized physically in A-site spinel materials.

83 e for the different performance of these two spinel materials.

84 e rind consisting of diopside, hedenbergite, spinel (MgAl(2)O(4)), nepheline, and forsterite.

85 Mn nanoparticles buried inside them to form spinel Mn-Co oxide nanoparticles partially embedded in t

86 Co(3)O(4) nanoparticles, a manganese-cobalt spinel MnCo(2)O(4)/graphene hybrid was developed as a hi

87 ree standing and carbon-free architecture of spinel MnCo2O4 oxide prepared using facile and cost effe

88 Spinel (modeled as Fe3O4), goethite (alpha-FeOOH), and f

89 The monolithically integrated spinel nanoarrays exhibit tunable catalytic performance

90 magnetic properties of mixed-valent inverse spinel NiCo2O4(NCO) thin films.

91 Here, magnetically soft epitaxial spinel NiZnAl-ferrite thin films with an unusually low G

92 cteristic order-disorder temperatures in 3-2 spinels (nominal charges Z(A) = 3 and Z(B) = 2) are appr

93 We also show that inversion in isometric spinel occurs by a similar process.

94 n mobility is possible in other chalcogenide spinels, opening the door for the realization of other m

95 for the halogenation of phenols using Cu-Mn spinel oxide as a catalyst and N-halosuccinimide as halo

96 In the presence of Cu-Mn spinel oxide B, both electron-withdrawing and electron-d

97 d the high electro-catalytic activity of the spinel oxide enables excellent performance of the oxygen

98 hybrids results in covalent coupling between spinel oxide nanoparticles and N-doped reduced graphene

99 tal bonds between N-doped graphene oxide and spinel oxide nanoparticles.

100 unique compound in that it is the only known spinel oxide superconductor.

101 r clusters stabilized on a defective ZnGa2O4 spinel oxide surface, providing hydrogen productivity of

102 The crystal structures of A(2)BO(4) spinel oxides are classified as either normal or inverse

103 Here, a descriptor study on the ORR/OER of spinel oxides is presented.

104 s, lithium-rich layered oxides, high-voltage spinel oxides, and high-voltage polyanionic compounds.

105 The TMO-like spinel phase also alleviates the electrolyte decompositi

106 (II) were removed by the formation of MFe2O4 spinel phase and partially through their structural inco

107 e formation of a subunit of the ZnCr(2)Se(4) spinel phase known to form as inclusions during peritect

108 ed to result from the breakdown of the gamma-spinel phase of olivine to magnesium-perovskite and magn

109 coupling with the dissociation of the gamma-spinel phase of olivine.

110 ed to the formation of a TiMn2 O4 (TMO)-like spinel phase resulting from the reaction of TiO2 with th

111 nce of Cr(III) results in the formation of a spinel phase that is a solid solution between magnetite

112 tings prevented surface-initiated layered-to-spinel phase transitions in coated materials which were

113 patterns confirmed the formation of the pure spinel phase without any impurities.

114 e scale, alloys must develop a scale without spinel phase.

115 s of Li-ion batteries with lithium manganate spinel positive and graphite negative electrodes chemist

116 e are metallic Fe and Fe-Si beads, aluminous spinel rinds on the Al-Cu-Fe alloys, and Al2O3 enrichmen

117 he transformation of (Mg,Fe)2SiO4 from gamma-spinel (ringwoodite) to (Mg,Fe)SiO3-perovskite and (Mg,F

118 In perovskite/spinel self-assembled oxide nanocomposites, the substrat

119 Three major classes are spinels, sheet-like layered structures, and three-dimens

120 variety of compositions adopt the isometric spinel structure (AB2O4), in which the atomic-scale orde

121 esized iron oxide nanoparticles have a cubic spinel structure as characterized by HRTEM, SAED, and XR

122 Inorganic compounds with the AB2X4 spinel structure have been studied for many years, becau

123 Consequently, the simple spinel structure is more complicated than previously tho

124 4)) nanoparticles (ca. 25 nm) of the inverse-spinel structure prepared by the hydrothermal method.

125 us Fe(3)O(4) with crystalline walls (inverse spinel structure) has been synthesized for the first tim

126 gnated as LT-LiCoO2) that adopts a lithiated spinel structure, as an inexpensive, efficient electroca

127 ement leads to an elegant description of the spinel structure, but represents an increase in complexi

128 tion of the framework, while maintaining the spinel structure, lambda-MnO(2).

129 t into the defect chemistry of ringwoodite's spinel structure, which not only accounts for a potentia

130 into nanocrystalline forms with the inverse spinel structure.

131 ing along the [110] direction in the inverse spinel structure.

132 in the tetrahedral sites of the gamma-Fe2O3 spinel structure.

133 with a significant amount of defects in the spinel structure.

134 report a well-defined cuboctahedral MgAl2O4 spinel support material that is capable of stabilizing p

135 ized at the surface of the ternary MgCuCr2O4-spinel support.

136 , resulting from strong interactions between spinel surface oxygens and epitaxial platinum {111} face

137 c pathways for the relaxation of disorder in spinel that are absent in pyrochlore.

138 compact and continuous nanocrystalline Co3O4 spinel that is impervious to phase transformation and im

139 ion resistance and disordering energetics in spinel, the opposite of that observed in pyrochlores.

140 -Fe(2)O(3) (corundum structure) to Fe(3)O(4) spinel then to gamma-Fe(2)O(3) by oxidation, while prese

141 has been used as a conducting layer for the spinel thin films based devices and the search for a p-t

142 tely an order of magnitude lower than in 2-4 spinels, thus explaining why typical 3-2 samples exhibit

143 hat the pressure and temperature of the post-spinel transformation in Mg2SiO4 is consistent with seis

144 The calorimetric entropy of the olivine-spinel transition in Fe(2)SiO(4) (-16 +/- 5 J/mol.K) is

145 Spinel transition metal oxides are important electrode m

146 Lithium-ion (Li-ion) batteries based on spinel transition-metal oxide electrodes have exhibited

147 en evolution reaction activities, making the spinel-type LT-Li0,5CoO2 a potential bifunctional electr

148 t our results will even impact other hydrous spinel-type materials, helping to understand properties

149 al conductivity and viscosity of water-based spinel-type MnFe2O4 nanofluid.

150 al synthesis of approximately 5.5 nm inverse spinel-type oxide Ga2FeO4 (GFO) nanocrystals (NCs) with

151 xygen that results in nanosized particles of spinel-type oxide LiMn(2)O(4), one of the leading cathod

152 tly theoretically predicted, some classes of spinel-type oxide materials can be intrinsically doped b

153 ndings underscore the potential relevance of spinel-type oxides as p-type transparent conductive oxid

154 s from PMS induced by a magnetic CuFe(2)O(4) spinel was studied.

155 surface is composed of a Co- and/or Ni-rich spinel with antisite defects.

156 triggers conversion of adsorbed Zn(II) into spinel Zn(II)1-xMn(II)xMn(III)2O4 precipitates at pH 7.5

157 rustrated magnetic interactions in the cubic spinel ZnCr(2)O(4).