京都大学 / 0048 / 新制・論文博士 / 博士(農学) / 乙第13055号 / 論農博第2839号 / 新制||農||1045(附属図書館) / 学位論文||H28||N5012(農学部図書室) / 33145 / (主査)教授 河田 照雄, 教授 保川 清, 教授 橋本 渉 / 学位規則第4条第2項該当 / Doctor of Agricultural Science / Kyoto University / DFAM

CoordenaÃÃo de AperfeÃoamento de Pessoal de NÃvel Superior / The mineralogical composition of the Beige Bahia (BB) limestone was characterized by petrographic analysis, XRD, total-rock (TR) chemical analysis, and SEM on figurative elements of lytic texture. The results demonstrated that this type of calcrete is dolomitic (dolomite > 10% in TR), reaching over 50% in its lumpy features. The matrix is primarily calcite, whereas quartz (< 5% TR) and palygorskite are the most common accessory minerals. The changing mechanisms of the BB, as a building covering, were investigated from the loss of brightness, using in natura polished boards in bench, for comparison with observations carried out in situ in a metropolitan coastal area (Recife-PE), under humid tropical climate. Tests of accelerated changeability involving atmospheres with saline saturation (NaCl) and in SO2, attacks by acid solutions (HCl, HNO3, H2SO4), rain water and sea water, were conducted according to the Brazilian Association of Technical Standards/ABNT or experimentally, involving in natura polished test specimen. By considering as critical a brightness intensity &#8804; 40, whether for test specimen or for applications carried out in situ, a reliable prediction is possible based on bench data. In most cases, this critical level is reached around the third testing cycle, corresponding to ten years in in situ changing conditions. The most active mechanisms were the gas chamber with SO2 saturation, and the sea water; and the critical brightness was reached between 2 and 2.5 cycles in bench. The set of results did not confirm if the ferric staining and black crusts are of lithogenic origin, whereas âwhite crustsâ are made of gypsum (CaSO4.H2O), by the reaction of H2SO4 with the calcite surface of the BB. Therefore, the inadequacy of the application of this product on external coverings is confirmed, particularly in the presence of sea spray or in metropolitan situations, where the atmosphere is mpregnated with SO2. / A composiÃÃo mineralÃgica do calcÃrio Bege Bahia (BB) foi caracterizada por anÃlise petrogrÃfica, DRX, anÃlises quÃmicas sobre rocha-total (RT), e MEV sobre elementos figurados da textura lÃtica. Os resultados demonstraram que este tipo de calcrete à dolomÃtico (dolomita > 10% em RT), atingindo mais de 50% em suas feiÃÃes grumosas. A matriz à essencialmente calcÃtica, enquanto quartzo (< 5% RT) e palygorskita sÃo os minerais acessÃrios mais frequentes. Os mecanismos de alteraÃÃo do BB, como revestimento de edificaÃÃes, foram investigados a partir da perda de brilho, utilizando-se placas lustradas in natura em bancada, para comparaÃÃo com observaÃÃes in situ em Ãrea litorÃnea metropolitana (Recife-PE), sob clima tropical Ãmido. Ensaios de alterabilidade acelerada envolvendo atmosferas com saturaÃÃo salina (NaCl) e em SO2, ataques por soluÃÃes Ãcidas (HCl, HNO3, H2SO4), Ãgua de chuva e Ãgua do mar, foram conduzidos segundo normas ABNT ou experimentalmente, envolvendo corpos de prova lustrados in natura. Considerando-se crÃtica uma intensidade de brilho &#8804; 40, seja para os corpos de prova quanto em aplicaÃÃes in situ, torna-se possÃvel uma confiÃvel prediÃÃo a partir dos dados de bancada. Na maior parte dos casos, este nÃvel crÃtico à atingido em torno do terceiro ciclo dos ensaios, correspondendo a 10 anos em condiÃÃes de alteraÃÃo in situ. Os mecanismos mais atuantes foram a cÃmara de gÃs com saturaÃÃo em SO2 e a Ãgua do mar, sendo o brilho crÃtico atingido entre 2 a 2,5 ciclos em bancada. O conjunto dos resultados nÃo confirmou se manchamentos fÃrricos e crostas negras sÃo de origem litogÃnica, enquanto que âcrostas brancasâ sÃo constituÃdas de gipsita (CaSO4.H2O), por reaÃÃo de H2SO4 com a superfÃcie calcÃtica do BB. Assim, confirma-se a inadequaÃÃo de aplicaÃÃo deste produto em revestimentos externos, particularmente em presenÃa de spray marinho ou situaÃÃes metropolitanas, onde a atmosfera apresenta-se impregnada com SO2.

No description available.

Obesity results from an excess of adipose tissue and is a major risk factor for type 2 diabetes, cardiovascular disease, and cancer. Adipose tissue exists in two main forms: white adipose tissue (WAT), which stores energy as triglycerides, and brown adipose tissue (BAT), which dissipates stored energy as heat. White adipose tissue is composed of several subcutaneous and visceral depots, each possessing distinct molecular and functional characteristics. Brown-like adipocytes can emerge in WAT depots in response to cold or beta-adrenergic stimulation. These cells have been called “beige” or “brite” (brown-in-white) cells. The reduction of obesity in mice treated with beta-adrenergic agonists is correlated with the emergence of beige cells. Beige cell development occurs most readily in subcutaneous depots, and to the least extent in visceral depots. Understanding the molecular mechanisms underlying beige cell development in different WAT depots may be important in discovering new therapies against obesity and related diseases. Our lab has previously discovered that Tyrosine Kinase 2 (Tyk2), an important mediator of cytokine signaling, promotes the development of classical brown adipose tissue. Due to the lack of functional BAT, Tyk2-knockout (Tyk2-/-) mice become grossly obese with age and develop several symptoms of the metabolic syndrome. In the present study, we have found a potential role of Tyk2 in the development of beige cells. Here, we show that mRNA expression of BAT-selective genes (UCP1, Cidea, Cox8b, and Elovl3) is significantly reduced in subcutaneous WAT of Tyk2-knockout (Tyk2-/-) mice compared to wild-type mice. Surprisingly, BAT-selective genes are induced in Tyk2-/- subcutaneous WAT by acute starvation. These findings suggest that Tyk2 is required for the development of beige cells under ambient conditions, and that the need for Tyk2 in beige cell development is bypassed during nutritional stress, a stimulus of the sympathetic response.

A atividade do complexo 1 da proteína alvo mecanístico da rapamicina (mTORC1), importante regulador da adiposidade e do metabolismo de lipídeos, está aumentada no tecido adiposo de camundongos obesos. A inibição completa de mTORC1 reduz a adiposidade, enquanto que sua inibição parcial potencializa a obesidade induzida por dieta. Assim, hipotetizamos que um nível ótimo de ativação de mTORC1 é necessário para promover aumento da adiposidade, de forma que sua superativação é tão inibitória para a deposição de gordura quanto sua inibição completa. Para testar esta hipótese, investigamos os efeitos da ativação constitutiva de mTORC1, induzida pela deleção de Tsc1, especificamente em adipócitos na adiposidade in vivo. A deleção de Tsc1 reduziu a massa do tecido adiposo visceral, mas não do subcutâneo, que foi associado ao aumento da lipólise e browning. Além disso, aumentou em ambos tecidos adiposos a massa e atividade oxidativa mitocondrial. Esses dados apoiam nossa hipótese de que é necessário um nível ótimo de ativação de mTORC1 para promover aumento da adiposidade. / The activity of mechanistic target of rapamycin complex 1 (mTORC1), an important regulator of adiposity and lipid metabolism, is increased in adipose tissue of obese mice. Complete mTORC1 inhibition reduces adiposity, whereas partial mTORC1 inhibition enhances diet-induced obesity. Therefore, we hypothesized that an optimal level of mTORC1 activity is required to increase adiposity, in such a manner that mTORC1 overactivation is as inhibitory to fat deposition as its complete inhibition. To test this hypothesis, we investigated the effects of constitutive mTORC1 activation, induced by Tsc1 deletion, specifically in adipocytes on adiposity in vivo. Tsc1 deletion reduced visceral, but not subcutaneous, fat mass, which was associated with increased lipolysis and browning. Moreover, it enhanced mitochondrial mass and oxidative activity in both visceral and subcutaneous fat. These data support our hypothesis that an optimal level of mTORC1 activation is necessary to increase adiposity.

A atividade do complexo 1 da proteína alvo mecanístico da rapamicina (mTORC1), importante regulador da adiposidade e do metabolismo de lipídeos, está aumentada no tecido adiposo de camundongos obesos. A inibição completa de mTORC1 reduz a adiposidade, enquanto que sua inibição parcial potencializa a obesidade induzida por dieta. Assim, hipotetizamos que um nível ótimo de ativação de mTORC1 é necessário para promover aumento da adiposidade, de forma que sua superativação é tão inibitória para a deposição de gordura quanto sua inibição completa. Para testar esta hipótese, investigamos os efeitos da ativação constitutiva de mTORC1, induzida pela deleção de Tsc1, especificamente em adipócitos na adiposidade in vivo. A deleção de Tsc1 reduziu a massa do tecido adiposo visceral, mas não do subcutâneo, que foi associado ao aumento da lipólise e browning. Além disso, aumentou em ambos tecidos adiposos a massa e atividade oxidativa mitocondrial. Esses dados apoiam nossa hipótese de que é necessário um nível ótimo de ativação de mTORC1 para promover aumento da adiposidade. / The activity of mechanistic target of rapamycin complex 1 (mTORC1), an important regulator of adiposity and lipid metabolism, is increased in adipose tissue of obese mice. Complete mTORC1 inhibition reduces adiposity, whereas partial mTORC1 inhibition enhances diet-induced obesity. Therefore, we hypothesized that an optimal level of mTORC1 activity is required to increase adiposity, in such a manner that mTORC1 overactivation is as inhibitory to fat deposition as its complete inhibition. To test this hypothesis, we investigated the effects of constitutive mTORC1 activation, induced by Tsc1 deletion, specifically in adipocytes on adiposity in vivo. Tsc1 deletion reduced visceral, but not subcutaneous, fat mass, which was associated with increased lipolysis and browning. Moreover, it enhanced mitochondrial mass and oxidative activity in both visceral and subcutaneous fat. These data support our hypothesis that an optimal level of mTORC1 activation is necessary to increase adiposity.

Materials chemistry basically deals with rational design and synthesis of new solids exhibiting various functional properties. A sound knowledge of crystal structures and chemical bonding is needed to understand the properties of materials. Space group, cell parameters and atomic positions provide a basic crystallographic description of the structure. Crystal structure could be described in a detailed way in terms of close packing of anions and occupancy of cations in different coordination sites. The coordination polyhedra and their interconnectivity bring out the interrelationships between different structures and the properties exhibited. Transition metals (TMs) are d-block elements which occupy groups 3-12 in Periodic Table. IUPAC defines a TM as ‘an element whose atoms have partially filled d-shell, or which can give rise to cations with an incomplete d-shell’. The partially filled d-shell in TMs plays an important role in various chemical and physical properties of TMs. Although TM cations can form compounds with different anions, most of the TM containing compounds are metal oxides due to the large free energies for formation of oxides. Binary TM oxides adopt different kinds of structures among which rock salt (e.g. NiO), rutile (e.g. TiO2), and corundum (e.g. Cr2O3) are most common. Ternary TM oxides are also known to form in variety of structures with the perovskite (e.g. BaTiO3), and the spinel (e.g. MgFe2O4) structures being well known. TM oxides exhibit a broad range of electronic and magnetic properties. TM oxides, at one end, display metallic behavior (e.g. ReO3, RuO2, LaNiO3) due to the delocalized electrons and at other end, show insulating behavior (e.g. NiO) due to the localized electrons. In between, TM oxides have semiconducting properties involving either the hopping of carriers (e.g. partially reduced TiO2, Nb2O5, WO3 and so on) or the electron excitation from the valence band to the conduction band (e.g. SnO2). TM oxides are known to have diverse magnetic properties: diamagnetic (e.g. TiO2, ZrO2), paramagnetic (e.g. VO2, NbO2), ferromagnetic (e.g. CrO2, La0.67Ca0.33MnO3), ferrimagnetic (e.g. Fe3O4, MnFe2O4) and antiferromagnetic (e.g. NiO, LaCrO3). TM oxides with partially filled 3d-shell are expected to be ‘metallic’ according to Bloch-Wilson theory, but in practice they are Mott insulators (localized 3d electrons) because of correlation energy (U) involved in the transfer of d-electrons between adjacent sites. Certain TM oxides also show insulator-metal (I-M) transitions induced by change of temperature, pressure or composition. For example, VO2 and Ba2IrO4 are known for their temperature and pressure induced I-M transitions, respectively. La1-xSrxCoO3 becomes metal at a particular Sr concentration being one of the examples for composition-dependent I-M transition. TM oxides are usually synthesized by conventional ceramic method in which stoichiometric mixture of starting materials is reacted at elevated temperatures. Multiple prolonged heating with intermittent grindings in ceramic method generally results in thermodynamically controlled products. The metastable phases which are of interest may not be obtained by ceramic method. Chimie douce/soft chemistry methods are generally adopted to stabilize the metastable phases. The guiding principle behind the chimie douce is to have kinetic control (rather than thermodynamic control) to realize metastable phases. Accordingly, metastable derivatives are obtained by choosing appropriate precursors, or adopting sol-gel and molten flux or ion exchange/intercalation methods. The present thesis is devoted to an investigation of transition metal oxides towards development of functional materials exhibiting visible light absorption/emission and lithium insertion/extraction for cathode materials in lithium ion battery. TM oxides find application as photovoltaic materials, luminescent emission materials, photocatalysts, light absorption/pigment materials and so on, based on their optical properties. Ferroelectric TM oxides with perovskite structure [Green coloured (KNbO3)1-x (BaNi1/2Nb1/2O3-δ)x] are studied currently as photovoltaic materials which show high open circuit voltage (Voc = 3.5 V) despite very low short circuit current (Vsc = 40 nA cm-2). TM oxides are also known to exhibit photoluminescent emission which could be due to the doping activator ions (e.g. MnII doped Zn2GeO4) or TM oxide (e.g. CaWO4) itself being self-activator. While the green and red emissions are common for TM oxides, blue emission is rare (e.g. Ar+ irradiated SrTiO3 is a blue emitter). Coloured TM oxides with band gap in visible region are employed as photocatalysts for solar water splitting (e.g. yellow BiVO4, yellow Ag3PO4, yellow TaON, red Fe2O3) and photo-oxidation of organic pollutants (e.g. TiO2-xNx and CaCu3Ti4O12). The coloured TM oxides also find application as pigments from early times, for example, Egyptian blue (CaCuSi4O10), Han blue (BaCuSi4O10), Han purple (BaCuSi2O6), Malachite green (Cu2CO3(OH)2), Ochre red (Fe2O3) and many others. A list of pigments based on TM oxides is given in Table 1. Pigment materials are applied as colouring materials in inks, dyes, paints, plastics, ceramics glazers, enamels and textiles. Table 1. List of TM oxide based pigments and their colours Pigment colour Compound White Titanium dioxide (TiO2) Black Iron oxide black (Fe3O4) Red Iron oxide red (Fe2O3), Ca1-xLaxTaO2-xN1+x (yellow-red) Orange Iron oxide orange (Fe2O3) Yellow Yellow ochre [FeO(OH)·H2O] Green Malachite green [Cu2CO3(OH)2], Viridian (Cr2O3. 2H2O), Y2BaCuO5 Blue Egyptian blue (CaCuSi4O10),Cobalt aluminate (CoAl2O4), YIn1-xMnxO3 Purple Han purple (BaCuSi2O6) Violet Cobalt phosphate [Co3(PO4)2] Colours of the TM oxides arise from visible light absorption due to the ligand field d-d electronic transitions. Though d-d transitions are parity forbidden, the selection rules get relaxed due to different reasons such as symmetry reduction (due to distortion) and vibronic couplings. The colour of the TM oxides is influenced mainly by two factors (i) oxidation state of TM ion present and (ii) ligand field around the TM ion produced by anion geometry. In order to develop new pigment oxides, our strategy was to choose colourless metal oxides having unusual (five coordinated geometry) or irregular/distorted (distorted octahedral/tetrahedral) coordination geometries around metal ion and produce coloured oxides by substituting 3d-TM ions at the metal ion site. We made a detailed study on the origin of the colour and pigment quality of the resulting coloured oxides. In the present thesis, which has two parts, the first part (Part 1) discusses the development of 3d-TM ion substituted coloured oxides with potential for pigment applications. Chapter 1.1 describes the purple inorganic pigment, YGa1-xMnxO3 (0 < x ≤ 0.10), based on the hexagonal YGaO3. The metastable series of oxides were prepared by a sol-gel technique where the dried gels, obtained from aqueous solutions of metal nitrates-citric acid mixtures, were calcined for a short duration in preheated furnace around 850°C/10 mins. The purple colour of the oxides arises from the specific trigonal bipyramidal ligand field around MnIII that obtains in the YGaO3 host. Other hexagonal RGaO3 hosts for R = Lu, Tm and Ho substituted with MnIII also produce similar purple coloured materials. In Chapter 1.2, we present a study on substitution of 3d-TM ions in LiMgBO3 host [where Mg(II) has a trigonal bipyramidal (TBP) oxygen coordination)]. We find that single-phase materials are formed for LiMg1-xCo(II)xBO3 (0 < x ≤ 1.0), LiMg1-xNi(II)xBO3 (0 < x ≤ 0.1), LiMg1-xCu(II)xBO3 (0 < x ≤ 0.1) and also Li1-xMg1-xFe(III)xBO3 (0 < x ≤ 0.1) of which the Co(II) and Ni(II) derivatives are strongly coloured, purple-blue and beige-red respectively, thus identifying TBP CoO5 and NiO5 as the new chromophores for these colours. Chapter 1.3 describes the synthesis, crystal structures and optical absorption spectra/colours of 3d-TM substituted α-LiZnBO3 derivatives: α-LiZn1-xMIIxBO3 [MII = CoII (0 < x < 0.50), NiII (0 < x ≤ 0.05) and CuII (0 < x 0.10)] and α-Li1+xZn1-2xMIIIxBO3 [MIII = MnIII (0 < x ≤ 0.10) and FeIII (0 < x 0.25)]. The crystal structure of the host α-LiZnBO3, which is both disordered and distorted with respect to Li and Zn occupancies and coordination geometries, is largely retained in the derivatives, giving rise to unique colours [blue for CoII, magenta for NiII and violet for CuII], that could be of significance for the development of new, inexpensive and environmentally-benevolent pigment materials, especially for the blue colour. Accordingly, the work indentifies distorted tetrahedral MO4 (M = Co, Ni, Cu) (together with a long M-O bond that gives a trigonal bipyramidal geometry) structural units as the new chromophores for the blue, magenta and violet colours respectively, in the α-LiZnBO3 host. In Chapter 1.4, we describe the synthesis, crystal structures and optical absorption spectra of 3d-TM substituted spiroffite derivatives, Zn2-xMxTe3O8 (MII = Co, Ni, Cu; 0 < x ≤ 1.0). The oxides are readily synthesized by solid state reaction of stoichiometric mixtures of the constituent binaries at 620°C/12h. Rietveld refinement of the crystal structures from powder XRD data shows that the Zn/MO6 octahedra are strongly distorted, as in the parent Zn2Te3O8 structure, consisting of five relatively short Zn/MII – O bonds (1.898 – 2.236 Å) and one longer Zn/MII– O bond (2.356 – 2.519 Å). We have interpreted the unique colors and the optical absorption/diffuse reflectance spectra of Zn2-xMxTe3O8 in the visible, in terms of the observed/irregular coordination geometry of the Zn/MII – O chromophores. We could not however prepare the fully-substituted M2Te3O8 (MII = Co, Ni, Cu) by the direct solid state reaction method. Density Functional Theory (DFT) modeling of the electronic structure of both the parent and the transition metal substituted derivatives provides new insights into the bonding and the role of transition metals toward the origin of color in these materials. We believe that transition metal substituted spiroffites Zn2-xMxTe3O8 reported here suggest new directions for the development of colored inorganic materials/pigments featuring irregular/distorted oxygen coordination polyhedra around transition metal ions. Red coloured materials are rare in nature. Li2MnO3 is a unique oxide with an unusual red colour imparted by MnIV ions. Chapter 1.5 describes a detailed experimental investigation of Li2MnO3 together with other related MnIV oxides that probes the red colour of Li2MnO3 as well as its photoluminescence. Optical absorption spectra reveal a strong band gap absorption with a sharp edge at ~ 610 nm and a transparent region between ~ 610 and ~ 650 nm that causes the red colour of Li2MnO3 samples. Octahedral MnIV ligand field transitions, corresponding to both MnIV at ideal sites and MnIV displaced to Li sites in the rock salt based layered structure of Li2MnO3, are observed in the excitation spectra of Li2MnO3 samples. Optical excitation at the ligand field transition energies produces tunable emission in the red-yellow-green region, rendering Li2MnO3 a unique MnIV oxide. The honeycomb ordered [LiMn6] units in the structure likely causes both the absorption and photoluminescence properties of Li2MnO3. Lithium containing TM oxides with rock salt related structure are being investigated extensively for application as next generation cathode materials for Lithium ion batteries (LIBs). Recent research is focused on lithium-rich layered oxides (LLOs) which are solid solutions between Li2MO3 (where M = Ti, Mn and Ru) and LiMO2 (where M = Cr, Mn, Fe, Co, Ni). LLOs have excess lithium in the TM layer in addition to lithium in lithium layer of rock salt derived structure. LLOs have gained attention because of their higher discharge capacity in the range of ~ 250 mAhg-1. While most of the LLOs investigated so far contain 3d-TM ions (Mn, Fe, Co, Ni), recently there has been an interest in the study of the role of ruthenium in addition to 3d-TM ions. We have investigated ruthenium containing LLOs with a view to probe (i) the role of ruthenium and (ii) the concentration of excess lithium in the TM layers in producing higher discharge capacities. The results are discussed in the Part 2 of the thesis.Li5NiMnRuO8(Li[Li0.25Ni0.25Mn0.25Ru0.25]O2) form in the Li2RuO3 crystal structure. Electrochemical studies indicate that the Co-containing oxides exhibit a higher initial discharge capacity (for e.g. ~ 180 mAhg-1 for Li4CoRuO6) as well as a higher reversible discharge capacity (~130 mAhg-1 for Li4CoRuO6) compared to the corresponding Ni-analogs. Participation of oxide ions (higher oxidation state of Ru) in the redox process could explain the higher discharge capacity during the first cycle. Reduced capacity (capacity fade) during the subsequent cycles could arise from the oxygen evolution due to the redox process (2O2- → 2O- → O2), which is not reversible. The present work shows that ruthenium incorporation in rock salt layered oxides along with Co/Ni appears to give a beneficial effect in producing a higher discharge capacity. In addition, the compounds crystallizing with the R-3m structure (related to LiCoO2) appear to give a better reversible capacity than the compounds crystallizing in the C2/c structures (Li2TiO3 and Li2RuO3).

No description available.

No description available.

No description available.