Provided is a backlight unit including a light source, an encapsulation layer, and a green quantum dot film. The light source emits a blue light. The encapsulation layer encapsulates the light source. The encapsulation layer includes red phosphors and yellow phosphors. The green quantum dot film is disposed above the light source and the encapsulation layer. The blue light is transmitted through the encapsulation layer and the green quantum dot film to generate a white light. A display device including the said backlight unit is also provided.

Provided is a backlight unit including a light source, an encapsulation layer, and a green quantum dot film. The light source emits a blue light. The encapsulation layer encapsulates the light source. The encapsulation layer includes red phosphors and yellow phosphors. The green quantum dot film is disposed above the light source and the encapsulation layer. The blue light is transmitted through the encapsulation layer and the green quantum dot film to generate a white light. A display device including the said backlight unit is also provided.

A powder for coating or sintering has a peak assigned to cubic Y.sub.3Al.sub.5O.sub.12 and a peak assigned to orthorhombic YAlO.sub.3 exhibited in X-ray diffractometry, and the intensity ratio of the peak assigned to the (112) plane of the orthorhombic YAlO.sub.3 to the peak assigned to the (420) plane of the cubic Y.sub.3Al.sub.5O.sub.12 is at least 0.01 and less than 1. Alternatively, a powder for coating or sintering includes a composite oxide of yttrium and aluminum, and the volume of pores with a pore size of from 0.1 to 1 μm of the powder is at least 0.16 mL/g. It is preferable that, in X-ray diffractometry using CuKα radiation with a scan range of 2θ=20° to 60°, a peak assigned to the cubic Y.sub.3Al.sub.5O.sub.12 is a peak that shows the highest peak intensity.

A powder for coating or sintering has a peak assigned to cubic Y.sub.3Al.sub.5O.sub.12 and a peak assigned to orthorhombic YAlO.sub.3 exhibited in X-ray diffractometry, and the intensity ratio of the peak assigned to the (112) plane of the orthorhombic YAlO.sub.3 to the peak assigned to the (420) plane of the cubic Y.sub.3Al.sub.5O.sub.12 is at least 0.01 and less than 1. Alternatively, a powder for coating or sintering includes a composite oxide of yttrium and aluminum, and the volume of pores with a pore size of from 0.1 to 1 μm of the powder is at least 0.16 mL/g. It is preferable that, in X-ray diffractometry using CuKα radiation with a scan range of 2θ=20° to 60°, a peak assigned to the cubic Y.sub.3Al.sub.5O.sub.12 is a peak that shows the highest peak intensity.

A material synthesis method may comprise: adding at least one liquid precursor solution to an atomizer device; generating by the atomizer device an aerosol comprising liquid droplets; transporting the aerosol to a reactive zone for evaporating one or more solvents from the aerosol; and collecting particles synthesized from at least evaporating the aerosol.

A material synthesis method may comprise: adding at least one liquid precursor solution to an atomizer device; generating by the atomizer device an aerosol comprising liquid droplets; transporting the aerosol to a reactive zone for evaporating one or more solvents from the aerosol; and collecting particles synthesized from at least evaporating the aerosol.

Disclosed is a method for preparing an alumina-based solid solution ceramic powder by using an aluminum oxygen combustion synthesis water mist process, which comprises: drying raw materials and then mixing same until uniform to obtain a mixed material; loading the mixed material into a high-pressure reactor, igniting same in an oxygen-containing atmosphere, carrying out a high-temperature combustion synthesis reaction to form a high-temperature melt and then carrying out heat preservation for 1-60 s; and then opening a nozzle, ejecting the high-temperature melt through the nozzle and rapidly cooling same through a liquid phase, thus obtaining the alumina-based solid solution ceramic powder.

Doped cerium oxide particles may comprise about 90 weight percent (wt. %) to about 99.9 wt. % cerium oxide (CeO.sub.2) and up to about 10 wt. % dopant. Exemplary doped cerium oxide particles may have a BET specific surface area of more than 150 m.sup.2/g after calcination at 500° C. for 8 hours. Exemplary doped cerium oxide particles may have an oxygen storage capacity (OSC) of more than 900 μmol.Math.O.sub.2/g after calcination at 500° C. for 8 hours.

To a co-precipitating aqueous solution, aqueous solutions containing (a) Tb ions, (b) at least one other rare earth ions selected from the group consisting of Y ions and lanthanoid rare earth ions (excluding Tb ions), (c) Al ions and (d) Sc ions are added; the resulting solution is stirred at a liquid temperature of 50° C. or less to induce a co-precipitate of the components (a), (b), (c) and (d); the co-precipitate is filtered, heated and dehydrated; and the co-precipitate is fired thereafter at from 1,000° C. to 1,300° C., thereby forming a sinterable garnet-type complex oxide powder.

To a co-precipitating aqueous solution, aqueous solutions containing (a) Tb ions, (b) at least one other rare earth ions selected from the group consisting of Y ions and lanthanoid rare earth ions (excluding Tb ions), (c) Al ions and (d) Sc ions are added; the resulting solution is stirred at a liquid temperature of 50° C. or less to induce a co-precipitate of the components (a), (b), (c) and (d); the co-precipitate is filtered, heated and dehydrated; and the co-precipitate is fired thereafter at from 1,000° C. to 1,300° C., thereby forming a sinterable garnet-type complex oxide powder.