KR101593470B1 - Glass composition for carrying phosphor and wave converter, light emitting device - Google Patents

Abstract

The present invention relates to a glass composition for supporting a phosphor capable of low-temperature firing and a wavelength conversion and a light-emitting device including the same. Phosphor carrying the glass composition according to the present invention is _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass comprising, in the SiO ₂ from 10 to 20mol%, the B ₂ O ₃ is The content of the Al ₂ O ₃ is from 0 to 5 mol%, the content of the ZnO is from 15 to 35 mol%, the content of the Na ₂ O is from 15 to 30 mol%, the molar ratio of SiO ₂ to Na ₂ O The ratio is 0.4 to 1.1, and the molar ratio of SiO _{2 to} ZnO is 0.4 to 0.6.

Description

Technical Field [0001] The present invention relates to a glass composition for supporting a phosphor, a wavelength converter, and a light emitting device including the phosphor composition.

The present invention relates to a glass composition for supporting a phosphor, a wavelength converter, and a light emitting device including the phosphor composition. More particularly, the present invention relates to a glass composition for supporting a phosphor capable of low-temperature firing, a wavelength converter, and a light-emitting device including the same.

The light emitting diode has advantages of high energy conversion efficiency, long life, low voltage driving, and no complicated driving circuit. Accordingly, light emitting diodes are expected to replace solid state lighting in the near future to replace conventional light sources such as incandescent, fluorescent and mercury lamps. Particularly, the white light emitting diode has a high utility value as a next generation light source.

In general, a light emitting diode can emit only monochromatic light having a narrow wavelength range in terms of its light emission principle. Therefore, in order to realize a white light emitting diode, it is necessary to combine light emitting diodes emitting two or more different colors, Or a technique of combining a light emitting diode and a wavelength converting material, for example, a fluorescent material, a semiconductor or a dye, or the like is used. Among them, a technique of using a wavelength converting material to mix white light of a converted wavelength with non-converted light to realize white light is generally used.

Phosphors are generally used among the wavelength converting materials. Phosphors such as silicate, YAG (yttrium aluminum garnet), TAG (terbium aluminum garnet), and nitride are used as the phosphors. These phosphors are prepared in powder form and supported on synthetic organic materials such as resin and silicon to be used as wavelength conversion materials. The organic synthetic resin as a conventional phosphor support has a problem that the material itself is yellowed or browned or deteriorated due to external factors such as ultraviolet rays and moisture and internal factors such as heat and light of the light emitting diode itself.

As a result, the reliability of the light emitting diode is lowered and the lifetime thereof is reduced, which limits its use. However, when an inorganic material is used as a support, the phosphor can be easily controlled as in the case of using an existing organic material, and problems such as discoloration and deterioration of the existing organic material can be improved.

However, in order to use glass as a phosphor carrier, a glass frit suitable for supporting a phosphor must be provided. For example, silicate-based and nitrite-based phosphors easily generate efficient charges due to the deterioration of active ions at high temperatures. Therefore, a glass frit for supporting a phosphor requires a firing temperature of 550 ° C or less, And must have high fluidity at the firing temperature to shorten the processing time and suppress the generation of bubbles. In addition, a high transmittance after firing can be used as a wavelength conversion material of a light emitting diode.

Conventional glass materials require a high firing temperature, which is disadvantageous in that the process cost is high and the usable phosphors are limited. In addition, in the case of a glass material capable of low-temperature firing among conventional glass materials, since the content of P ₂ O ₅ is high, the chemical stability is lowered and it is difficult to improve the permeability after firing.

Accordingly, development of a thermally and chemically stable glass material capable of being fired at a temperature of 550 DEG C or less is required.

SiO ₂ -B ₂ O ₃ -based glass, SiO ₂ -B ₂ O ₃ -BaO-based glass, and ZnO-B ₂ O ₃ -SiO ₂ -based glass disclosed in Japanese Patent Application Laid-Open No. 2008-255362 have high firing temperatures, It is difficult to apply the method. In addition, SnO-P ₂ O ₅ -B ₂ O ₃ glass and P ₂ O ₅ -ZnO-SiO ₂ glass disclosed in Korean Patent Laid-Open Nos. 10-2009-0026754 and 10-2013-0127716 Although low-temperature firing is possible, P ₂ O ₅ must be contained in an amount of 40 mol% or more. In this case, mass production is difficult in the manufacturing process due to high hygroscopicity of P ₂ O ₅ , and the manufactured glass has a problem of long-term durability because of its poor chemical durability. In addition, in order to produce glass frit, a grinding step is generally carried out. Glass containing a large amount of P ₂ O ₅ may cause coloration and foreign matter inflow due to chemical reaction with the atmosphere during milling. Therefore, transparency is a problem in glass containing a large amount of P ₂ O ₅ .

Japanese Patent Application Laid-Open No. 2008-255362 Korean Patent Publication No. 10-2013-0127716 Korean Patent Publication No. 10-2009-0026754

A problem to be solved by the present invention is to provide a glass composition for supporting a phosphor having high stability and reliability.

Another object of the present invention is to provide a glass composition for supporting a phosphor having a low firing temperature, specifically, a glass composition for supporting a phosphor having a firing temperature of 550 캜 or less.

Another object of the present invention is to provide a thermally and chemically stable glass composition for supporting a phosphor.

Another object of the present invention is to provide a glass composition for supporting a phosphor having low hygroscopicity and low possibility of phase separation.

Another object of the present invention is to provide a glass composition for supporting a phosphor capable of supporting various kinds of phosphors.

Another object of the present invention is to provide a glass composition for supporting a phosphor having improved sensitivity and mass productivity of process conditions.

Another object of the present invention is to provide a wavelength converter including the glass composition for supporting a phosphor, and to provide a light emitting device having improved reliability and a long lifetime.

But phosphor carrying a glass composition in accordance with one embodiment of the present invention include _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass, the SiO ₂ is from 10 to 20mol%, the B ₂ O ₃ is 30 to to 40mol%, the Al ₂ O ₃ is from 0 to to 5mol%, the ZnO is 15 to 35mol%, and the Na ₂ O is contained by 15 to 30mol%, for the Na ₂ O The molar ratio of SiO ₂ to SiO ₂ may be 0.4 to 0.6, and the molar ratio of SiO _{2 to} ZnO may be 0.4 to 0.6. Since the glass composition for supporting a phosphor according to the present invention does not contain P ₂ O ₅ and SnO, the sensitivity of the manufacturing process is improved, and the chemical and thermal stability of the produced glass is high, thereby improving the reliability.

The firing temperature may be 550 캜 or lower.

Further, any one selected from MgO, WO ₃ , SrO _, BaO, Al ₂ O _3, Y ₂ O ₃ , Ga ₂ O ₃ , In ₂ O ₃ , WO ₃ , GeO ₂ and La ₂ O ₃ , Can contain more

Further, it further includes R ₂ O, wherein R is any one of Li, Na, K, Rb, and Cs, and R ₂ O may include 20 mol% or less.

The wavelength converter according to an embodiment of the present invention may include the above-described glass composition for supporting a phosphor; And a phosphor supported on the glass composition.

Further, the phosphor may be a YAG-based phosphor, a TAG-based phosphor, a silicate-based phosphor, a nitride-based phosphor, a fluoride-based phosphor, an oxysulfide-based phosphor, an oxynitride- Based phosphor, an oxyfluoride-based phosphor, or a combination thereof.

A light emitting device according to an embodiment of the present invention includes a light emitting diode; And a wavelength converter for converting a wavelength of light emitted from the light emitting diode, wherein the wavelength converter comprises the glass composition for supporting a phosphor according to any one of claims 1 to 4; And a phosphor supported on the glass composition.

A wavelength converter manufacturing method in accordance with one embodiment of the present invention, _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit, and mixing the phosphor, a predetermined mixed the glass frit, and the phosphor of plastic, including, but that the sintering temperature, the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit is, the SiO ₂ is between 10 to 20mol%, the B ₂ O ₃ is 30 to 40 mol% of Al ₂ O ₃ , 0 to 5 mol% of Al ₂ O ₃ , 15 to 35 mol% of ZnO, and 15 to 30 mol% of Na ₂ O.

In addition, the calcination may be performed in an atmospheric or reduced atmosphere.

Further, the firing temperature may be 550 DEG C or less.

But the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit further comprises the R ₂ O, and wherein R is any one of Li, Na, K, Rb and Cs, wherein R ₂ O may be contained in an amount of 20 mol% or less.

The glass composition for supporting a phosphor according to the present invention is capable of uniformly supporting a phosphor, has low coloration and high transmittance, can be chemically and physically stable and can effectively suppress the generation of denaturation, discoloration and deterioration, High and long-lasting. In addition, the phosphor-supported glass composition according to the present invention can be fired at a temperature of 550 ° C or less, so that the process applicability is excellent, and a wavelength converter can be manufactured by applying various phosphors.

The wavelength converter according to the present invention is low in hygroscopicity and high in fluidity at low temperatures since the glass composition for supporting a phosphor does not contain SnO and P ₂ O ₅ . Further, the manufacture of the wavelength changer can be performed in an atmospheric atmosphere or a reducing atmosphere, thereby facilitating the production process.

Further, since the light emitting device according to the present invention includes the wavelength converter and the glass composition for supporting the phosphor, the reliability is improved and it can be used for a long time.

1 is a cross-sectional view illustrating a light emitting device according to an embodiment of the present invention.
2 is a cross-sectional view illustrating a light emitting device according to another embodiment of the present invention.
3 is a cross-sectional view illustrating a light emitting device according to another embodiment of the present invention.

Hereinafter, embodiments of the present invention will be described in detail with reference to the accompanying drawings. In the drawings, the same reference numerals are used to designate the same or similar components throughout the drawings. In the following description of the present invention, a detailed description of known functions and configurations incorporated herein will be omitted when it may make the subject matter of the present invention rather unclear. In addition, exemplary embodiments of the present invention will be described below, but the technical spirit of the present invention is not limited thereto, and various modifications may be made by those skilled in the art.

First, a glass composition for supporting a phosphor according to an embodiment of the present invention will be described in detail.

Glass composition for a phosphor bearing is _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass and _{including, SiO 2 -B 2 O 3- Al} 2 O 3 -ZnO-Na 2 O -based glass SiO ₂ is 10 to 20 mol%, B ₂ O ₃ is 30 to 40 mol%, Al ₂ O ₃ is 0 to 5 mol%, ZnO is 15 to 35 mol%, and Na ₂ O is 15 to 30 mol% can do. Since the glass for supporting a phosphor having the above composition ratio does not contain SnO and P ₂ O ₅ , the hygroscopicity is low and the fluidity at low temperature is high, so that the firing process becomes easy. This will be described later in detail.

The _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O-based glass has a sintering temperature may be up to 550 ℃. The use of the glass that can be fired at such a low temperature facilitates the firing step and can also be used as a support for phosphors, such as silicate-based phosphors and nitride-based phosphors, whose efficiency is lowered due to denaturation of active ions at high temperatures.

In addition, the glass composition for supporting a phosphor does not contain SnO and P ₂ O ₅ , which can improve hygroscopicity and fluidity in a firing step and reduce the limit of the process atmosphere. For example, the low-temperature fired glass composition for supporting a phosphor may be fired in an air atmosphere or a reducing atmosphere.

SiO _{2, which} is included in the glass composition for supporting a phosphor, is one of the glass network formers and can form a three-dimensional network structure in the glass. Through this, the stability of the glass can be enhanced. However, as the SiO ₂ content increases, the softening point (Tg) increases and the viscosity increases.

Accordingly, the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass that contains a fluorescent material supporting the glass composition of the example of the present invention comprises from 10 to 20mol% of SiO _{2. SiO 2 -B 2 O 3- Al 2} O 3 When the -ZnO-Na ₂ O-based glass including SiO ₂ is less than 10mol% may decrease the stability of the glass, SiO ₂ -B ₂ O _3- Al ₂ O ₃ -ZnO-Na ₂ O-based glass contains SiO ₂ in an amount exceeding 20 mol%, the viscosity is increased and the fluidity is insufficient, so that the glass is difficult to be fired.

B ₂ O _3, which is included in the glass composition for supporting a phosphor, is one of the glass network formers and can form one-dimensional or two-dimensional and three-dimensional basic structures in glass. Glass containing B ₂ O ₃ can increase the flowability of the glass during firing, thereby facilitating the manufacturing process. However, as the B ₂ O ₃ content increases, the chemical durability of the glass can be weakened.

Accordingly, the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass that contains a fluorescent material supporting the glass composition of the example of the present invention comprises a B ₂ O ₃ from 30 to 40mol% . If the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass contains B ₂ O ₃ to 40mol% excess There can cause phase separation of the glass, it is possible to lower the chemical stability of the glass . On the other hand, if the produced _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass contains B ₂ O ₃ is less than 30mol% there is increased when the content of SiO _2, the flowability of the glass off The process becomes disadvantageous.

Al ₂ O ₃ contained in the glass composition for supporting a phosphor can serve as a mesh modifier for cutting off the mesh structure when the content thereof is high. When the content is low, Al ₂ O ₃ , together with SiO ₂ and B ₂ O ₃ , Can be formed. In addition, Al ₂ O ₃ serves to _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based and stabilize the glass, lower the thermal expansion coefficient.

_{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass comprising a glass composition for a phosphor bearing according to an embodiment of the present invention include Al ₂ O ₃ from 0 to 2mol%. If the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass is contained by the Al ₂ O ₃ greater than 2mol%, the fluidity of the glass becomes small, there may occur phase separation.

ZnO contained in the glass composition for supporting a phosphor can serve as a mesh modifier for cutting off the network structure, and when the content is high, a glass structure can be formed together with a part of SiO ₂ . ZnO can stabilize the glass and lower the thermal expansion coefficient of the glass. Accordingly, the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass that contains a fluorescent material supporting the glass composition according to the embodiment of the present invention, comprising 15 to 35mol% of ZnO, the ZnO The molar ratio of SiO ₂ to SiO ₂ may range from 0.4 to 0.5.

If the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass contains ZnO in 15mol%, there is a phase separation may occur easily. If the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass comprises more than 35mol% of ZnO there may be difficult to form the glass. _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass, the phase separation is likely to occur if at the same time as comprising 15 to 35mol% of ZnO, less than a molar ratio of SiO ₂ to ZnO 0.4 And the stability of the glass may be deteriorated. If the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass is at the same time as comprising 15 to 35mol% of ZnO, the molar ratio of SiO ₂ to ZnO is greater than 0.6, the glass is crystallized Or may crystallize upon firing, and the flowability of the glass may be deteriorated and the manufacturing process may be disadvantageous.

Na ₂ O, which contains a glass composition for carrying a phosphor is _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based to break the mesh consisting of SiO ₂ and B ₂ O _3, including a glass transition The temperature Tg and the softening point Ts can be lowered. Accordingly, it is possible to increase the fluidity of the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass. _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass comprising a glass composition for a phosphor bearing according to an embodiment of the present invention may comprise Na ₂ O 15 to 30mol%, The molar ratio of SiO ₂ to Na ₂ O may range from 0.4 to 0.6.

If the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass contains Na ₂ O is less than 15mol%, the glass forming difficult, can drop the fluidity of the glass. In the case of _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass contains Na ₂ O to 30mol% excess, may cause phase separation of the glass.

_{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass also contains 15 to 30mol% of Na ₂ O and at the same time, is less than a molar ratio of SiO ₂ to Na ₂ O of 0.4, the , Phase separation of the glass is liable to occur, and the firing temperature of the glass may increase. _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass is at the same time as include Na ₂ O into 15mol% to about 30mol%, the molar ratio of SiO ₂ to Na ₂ O is greater than 0.5 , The flowability and stability of the glass are deteriorated, and coloring can easily occur after the glass firing.

Na ₂ O may be included further a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based additional or alternatively on the glass. Na ₂ O is a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based alternative to a part of SiO ₂ in the glass, but is not limited to this.

Further, the glass composition for supporting a phosphor according to this embodiment may further include R ₂ O. The R may be any one of Li, Na, K, Rb, and Cs. R ₂ O may be included as a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based additional or alternatively on the glass. R ₂ O is a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O-based glass or SiO ₂ may be included to replace some of ZnO, but is not limited to such.

When R ₂ O replaces SiO ₂ , crystallization of the glass may occur during firing or crystallization of the glass composition may occur after firing. When R ₂ O replaces ZnO, the flowability at a given firing temperature of the glass can be improved. Thus the process can be improved applicability By the SiO ₂ is further included _{-B 2 O 3- Al 2 O 3} -ZnO-Na 2 O -based R ₂ O in the glass.

R ₂ O is a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based to break the mesh formed of SiO ₂ and B ₂ O ₃ in the glass transition temperature (Tg) and softening point (Ts) . Accordingly, when the glass is sintered, the fluidity can be increased. If the flowability during firing is increased, the glass can be easily molded, the occurrence of bubbles is reduced, and the light transmittance of the glass can be improved. Accordingly, the present invention can be applied to various light emitting devices, and can be easily applied to a manufacturing process of a light emitting device.

_{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass comprising a glass composition for a phosphor bearing according to an embodiment of the present invention may comprise a R ₂ O to less than 20mol%, 20mol %, The stability of the glass is deteriorated, so that the yield of the glass after firing is lowered and the glass composition can be easily generated.

Further, the phosphor-supported glass composition according to the present embodiment is _{MgO, WO 3, SrO, BaO} , Al 2 O 3, Y 2 O 3, Ga 2 O 3, In 2 O 3, GeO 2, and La ₂ O ₃ , Or any combination thereof. _{MgO, WO 3, SrO, BaO} , Al 2 O 3, Y 2 O 3, Ga 2 O 3, In 2 O 3, GeO 2, and La ₂ O ₃ is a _{SiO 2 -B 2 O 3 -Al 2} O 3 to improve the stability of Na ₂ O-based glass--ZnO may improve process applicability of the firing step. _{MgO, WO 3, SrO, BaO} , Al 2 O 3, Y 2 O 3, Ga 2 O 3, In 2 O 3, GeO 2, and La ₂ O ₃ is the _{SiO 2 -B 2 O 3 -Al 2} O _3- ZnO-Na ₂ O-based glass may be further contained in an amount of 0 to 5 mol%, and if it is contained in an amount exceeding 5 mol%, crystallization of the glass may occur and flowability may be deteriorated and processability may be impaired. However, it is not limited to the above range.

SiO ₂ -B ₂ O ₃ -Al ₂ O ₃ -ZnO-Na ₂ O glass is a transition metal such as Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Mo, Sn, Sb or Bi It may not contain oxides. The transition metal may cause a phenomenon of visible light absorption due to electron transition, which may cause the phenomenon of coloring of the glass, thereby lowering the transmittance of the glass composition for supporting the phosphor. However, the scope of the present invention is not limited thereto.

1 to 3 are sectional views for explaining a light emitting device according to embodiments of the present invention.

1, the light emitting device includes a main body 10, a first lead 11, a second lead 12, a side wall 13 integrally formed with the main body 10 , a light emitting diode 21, A wire 14 electrically connecting the light emitting diode 21 and the second lead 12, and a wavelength converter 30.

A side wall 13 can be disposed on the upper surface of the main body 10 and a cavity is provided in which the light emitting diode 21 can be mounted on the main body 10 surrounded by the side wall 13. [ The main body 10 and the side wall 13 may be formed of a polymer resin, ceramic, or the like, and the material thereof is not limited. In addition, the main body 10 may further include a heat sink (not shown) for discharging heat generated from the light emitting diodes 21.

The side wall 13 forming the cavity may be provided to have a predetermined inclination, and further, a reflector (not shown) may be further formed on the side wall 13 having the inclination. The reflector may reflect light emitted from the light emitting diode 21 to improve light extraction efficiency.

The first lead 11 and the second lead 12 may be electrically connected to the light emitting diode 21 and may be connected to an external power source. The first and second leads 11 and 12 may be disposed opposite to each other and protrude from the side surface of the main body 10 but the present invention is not limited thereto. And may be projected to the outside through vias passing through the upper and lower portions. The first lead 11 and the second lead 12 are not limited as long as they are conductive materials, and may be formed of a metal or an alloy including Cu or Al, for example.

The light emitting diode 21 is mounted in the cavity formed by the body 10 and the side wall 13 and can be formed in contact with the first lead 11. [ At this time, the light emitting diode 21 and the first lead 11 may be bonded to each other with a conductive adhesive agent such as Ag epoxy. In addition, the light emitting diode 21 and the second lead 12 may be electrically connected through the wire 14.

The form of electrical connection between the light emitting diode 21 and the leads 11 and 12 is not limited to that described above. For example, the light emitting diode 21 may be formed to be adhered to the main body 10, and the light emitting diode 21 and the first lead 11 may be electrically connected to each other through a wire (not shown) .

The shape of the light emitting diode 21 is not limited, and may be, for example, a horizontal light emitting diode or a vertical light emitting diode.

On the other hand, a wavelength converter 30 including a glass composition 31 for supporting a phosphor and a phosphor 32 is formed in the cavity. The wavelength converter 30 changes a part of the wavelength of the light emitted from the light emitting diode 21 so that light of a different wavelength is emitted to the outside. Accordingly, the light emitting device according to the present embodiment can emit light of various colors by mixing lights of various different wavelengths.

The wavelength converter 30 is formed by supporting a phosphor 32 on a phosphor composition 31 for supporting a phosphor. Since the phosphor 32 is supported on glass instead of a material such as an organic synthetic resin, the wavelength converter 30 is not discolored, denatured, or deteriorated by internal or external factors. Therefore, the light emitting device according to the present invention including the wavelength converter 30 can have high reliability and a long lifetime. Also, the light efficiency can be increased, and thus it can be used as a high-power light emitting source or illumination. However, the present invention is not limited thereto.

The phosphor 32 may be any one selected from the group consisting of a YAG-base phosphor, a TAG-base phosphor, a silicate-base phosphor, a nitride-base phosphor, a fluoride-base phosphor, an oxysulfide-base phosphor, an oxynitride-base phosphor, and an oxyfluoride-base phosphor. The glass composition 31 for supporting a phosphor on which the phosphor 32 is supported may have a sintering temperature of 550 DEG C or lower and various phosphors may be used. Therefore, the phosphor that can be supported is not limited to the above-described phosphors.

Next, referring to FIG. 2, the light emitting device according to the present embodiment is substantially similar to the light emitting device described with reference to FIG. 1, but differs from the light emitting device further including the sealing portion 15. Hereinafter, only differences will be described.

The light emitting device includes an encapsulating portion 15 in the cavity and a wavelength converter 40 formed on the encapsulating portion 15 and including a glass composition 41 for supporting a phosphor and a phosphor 42. The sealing portion 15 may be formed of epoxy, silicone, or glass material. The wavelength converter 40 may be formed on the sealing portion 15 in a film form. However, the present invention is not limited to this, and may be formed in the sealing portion 15.

3, the light emitting device according to the present embodiment is generally similar to the light emitting device described with reference to FIG. 2, except that the wavelength converter 50 including the glass composition 51 for supporting the phosphor and the fluorescent material 52 emits light And is formed by being adhered to the diode 21.

The wavelength converter 50 may be formed on the upper surface of the light emitting diode 21 as shown in FIG. 3 and may further be formed on the side surface of the light emitting diode 21.

In the present embodiments, the light emitting device has been described as a surface mount type (SMD type). However, the present invention is not limited to this, and a light emitting device of a through-hole technology (THT) package, Can be applied.

Next, a method of manufacturing a wavelength converter according to an embodiment of the present invention will be described in detail.

In the method of manufacturing a wavelength converter according to an embodiment of the present invention, SiO ₂ is 10 to 20 mol%, B ₂ O ₃ is 30 to 40 mol%, Al ₂ O ₃ is 0 to 5 mol%, ZnO is 15 to 35 in mol%, and, and Na ₂ O is contained in 15 to 30mol%, a molar ratio of SiO ₂ to Na ₂ O is 0.4 to 1.1, SiO ₂ for the molar ratio of SiO ₂ to ZnO satisfies 0.4 to 0.6 B ₂ O ₃ -Al ₂ O ₃ -ZnO-Na ₂ system glass frit and a phosphor, and firing the mixed glass frit and the phosphor at a predetermined firing temperature.

The firing may include molding the glass frit and the phosphor mixture by heating, but the present invention is not limited thereto. For example, the firing may further include pressing. In addition to the above methods, various types of firing are possible. Hereinafter, the manufacturing method will be described in detail, for example.

The wavelength converter manufacturing method is performed by, for example, weighing and mixing the target amounts of the glass frit and the phosphor. At this time, they may be mixed using a solvent, and the solvent may be ethanol. Thereafter, the glass frit and the phosphor are uniformly mixed using a milling process, and the milling process can be performed using, for example, a ball miller. Then, the mixed glass frit and the fluorescent material mixture are melted by heating at the predetermined firing temperature, cooled and then cooled to provide the wavelength converter. The molding step and the heating and melting step may be performed at the same time, and the pressing and pressing may be further included.

The glass frits to SiO ₂ is from 10 to 20mol%, B ₂ O ₃ is 30 to to 40mol%, Al ₂ O ₃ is from 0 to 5mol%, of ZnO is 15 to 35 mol%, Na ₂ O 15 to 30 mol%, the molar ratio of SiO ₂ to Na ₂ O is 0.4 to 1.1, and the molar ratio of SiO _{2 to} ZnO is 0.4 to 0.6, so that crystallization of the glass occurs during the firing of the glass frit Phase separation does not occur, and the hygroscopicity is low, thereby facilitating the process. Further, the glass composition fired from the glass frit has a high transparency.

Since the glass frit does not contain P ₂ O ₅ and SnO, the stability of the glass frit is high, and the glass composition can be stably formed in the firing process. Further, the glass frit not containing SnO can be fired in an atmospheric atmosphere or a reducing atmosphere. On the other hand, since the glass frit does not contain P ₂ O ₅ , hygroscopicity can be improved.

As described above, the glass frit containing no SnO and P ₂ O ₅ is easy to process and has excellent glass stability and transparency of the fired glass composition.

The predetermined firing temperature may be 550 DEG C or less. Show high fluidity the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit is below 550 ℃ has the advantage that the mass productivity is improved by facilitating the process at a temperature not higher than 550 ℃. Further, various phosphors such as YAG-base phosphors, TAG-base phosphors, silicate-base phosphors, nitride-based phosphors, Fluoride-based phosphors, including fluorophores which can be fired at 550 ° C or less, The phosphor, the oxysulfide-based phosphor, the oxynitride-based phosphor, and the oxyfluoride-based phosphor may be mixed together to form a wavelength converter. The phosphor included in the wavelength converter is not limited to this, and other phosphors capable of being fired at the predetermined firing temperature may be included.

Meanwhile, the wavelength converter according to the present embodiment may further include R ₂ O, and R may be any of Li, Na, K, Rb, and Cs. R ₂ O is the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit can additionally contain a further, or the R ₂ O is replaced by a portion of the SiO ₂ or the ZnO .

The _{R 2 O (R = Li,} Na, K, Rb, or Cs) is formed in the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass as B ₂ O ₃ and SiO ₂ The mesh is cut off to lower the glass transition temperature (T _g ) and the softening point (T _s ) to increase the fluidity during firing of the glass frit. When the flowability during firing is increased, the glass frit is easily formed, bubbles are less generated, light transmittance can be improved, and various light emitting devices can be applied to improve process applicability.

_{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit according to one embodiment of the present invention, it is preferable to further comprises the R ₂ O 0 to 20 mol%, 20mol% The stability of the glass frit may be deteriorated and the yield of the glass after firing may be lowered and coloring of the glass composition after firing may occur more easily.

Wherein R ₂ O is the _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based further on a glass frit, or may generally be further included, in which the R ₂ O is a part or all of the ZnO But it is not limited thereto. When the R ₂ O substitutes for SiO ₂ , crystallization of the glass frit may occur during firing or crystallization of the glass composition may occur after firing, whereas when the R ₂ O substitutes for ZnO, the glass phase of the glass frit Can be stabilized, and the fluidity at the predetermined firing temperature can be improved. Therefore, it is possible to improve the applicability of the process whereby R ₂ O is further comprising a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass frit.

In the meantime, in the method of manufacturing a wavelength converter according to the present embodiment, the glass frit may include at least one of MgO, WO ₃ , SrO, BaO, Al ₂ O ₃ , Y ₂ O ₃ , Ga ₂ O ₃ , In ₂ O ₃ , GeO ₂ , And La ₂ O ₃ , or a combination thereof. _{MgO, WO 3, SrO, BaO} , Al 2 O 3, Y 2 O 3, Ga 2 O 3, In 2 O 3, GeO 2, and La ₂ O ₃ is a _{SiO 2 -B 2 O 3 -Al 2} O 3 to improve the stability of -ZnO-Na ₂ O-based glass frit can improve process applicability of the firing step.

_{MgO, WO 3, SrO, BaO} , Al 2 O 3, Y 2 O 3, Ga 2 O 3, In 2 O 3, GeO 2, and La ₂ O ₃ is the _{SiO 2 -B 2 O 3 -Al 2} O _3- ZnO-Na ₂ O-based glass frit is preferably contained in an amount of 0 to 5 mol%, and when it is contained in an amount exceeding 5 mol%, crystallization of the glass may occur and flowability may be deteriorated, have. However, it is not limited to the above range.

In addition, the glass frit of SiO ₂ -B ₂ O ₃ -Al ₂ O ₃ -ZnO-Na ₂ O is a glass frit such as Ti, V, Cr, Mn, Fe, Co, Ni, Cu, Mo, Sn, Sb or Bi It is preferable that it does not contain an oxide of a transition metal. The transition metal may cause a phenomenon of visible light absorption due to electron transition, which may cause the coloring phenomenon of the glass frit, which may lower the transmittance of the glass composition after firing. However, the scope of the present invention is not limited thereto.

Hereinafter, specific experimental examples according to the present invention will be described in detail with reference to the tables.

Experimental Example 1

SiO ₂ -B ₂ O ₃ -Al ₂ O ₃ -ZnO-Na ₂ O glass is weighed by composition according to each sample as shown in the following table.

Unit: mol% Glass sample SiO ₂ B ₂ O ₃ ZnO Na ₂ O Al ₂ O ₃ SiO ₂
/ Na ₂ O SiO ₂
/ ZnO Melting result 550 ℃
Firing result Remarks One 20 30 32.5 17.5 0 1.1 0.6 O O 2 20 30 25 25 0 0.8 0.8 △ X Misting 3 20 30 20 30 0 0.7 One O X Misting 4 20 30 17.5 32.5 0 0.6 1.1 O No flow No flow 5 15 30 41.25 13.75 0 1.1 0.4 X - Phase separation 6 15 30 37 18 0 0.8 0.4 X - Phase separation 7 15 30 33 22 0 0.7 0.5 X - Phase separation 8 15 30 27.5 27.5 0 0.5 0.5 △ X No flow 9 15 30 22 33 0 0.5 0.7 △ X No flow 10 15 30 18 37 0 0.4 0.8 △ X No flow 11 15 30 13.75 41.25 0 0.4 1.1 △ X No flow 12 15 35 23 25 2 0.6 0.7 △ X No flow 13 15 30 25.5 27.5 2 0.5 0.6 O O 14 15 30 23 30 2 0.5 0.7 O △ No flow 15 15 28 27.5 27.5 2 0.5 0.5 O △ No flow 16 15 28 26.5 28.5 2 0.5 0.6 O △ No flow 17 15 28 25.5 29.5 2 0.5 0.6 X - Phase separation 18 15 30 28 25 2 0.6 0.5 O O 19 13 30 27.5 27.5 2 0.5 0.5 O No flow No flow 20 13 30 26.5 28.5 2 0.5 0.5 X Phase separation Phase separation 21 13 30 25.5 29.5 2 0.4 0.5 O O 22 13 28 29.5 27.5 2 0.5 0.4 X - Phase separation 23 13 28 28.5 28.5 2 0.5 0.5 X - Phase separation 24 13 28 27.5 29.5 2 0.4 0.5 X - Phase separation 25 13 28 26.5 30.5 2 0.4 0.5 X - Phase separation 26 13 28 25.5 31.5 2 0.4 0.5 X - Phase separation 27 10 35 28 25 2 0.4 0.4 X - Phase separation 28 10 30 33 25 2 0.4 0.3 X - Phase separation 29 10 40 23 25 2 0.4 0.4 O O

(Melting result: O - excellent,? Normal, X - crystallized or unmelted)

(Firing result: O - excellent,? Normal, X - crystallized or not formed)

Table 1 shows the results of melting and firing by composition of SiO ₂ -B ₂ O ₃ -Al ₂ O ₃ -ZnO-Na ₂ O glass according to the present invention. The first vertical line in Table 1 represents the number of the glass sample, the second vertical line represents the molar ratio (mol%) of SiO ₂ , the third vertical line represents the molar ratio (mol%) of B ₂ O ₃ , (mol%), the fifth vertical line is the molar ratio (mol%) of Na ₂ O, the sixth vertical line is the molar ratio (mol%) of Al ₂ O ₃ and the seventh vertical line is the molar ratio of SiO ₂ to Na ₂ O The molar ratio of SiO ₂ to ZnO in the eighth vertical line, the melting result in the ninth vertical line, the firing result in the tenth vertical line, and the test results of the glass sample in the eleventh vertical line are shown briefly.

In the results of the melting of Table 1, the symbol O indicates that it has been melted to good, the symbol Δ indicates that it is normally melted, and the symbol X means that it has not been crystallized or melted. In the results of the firing in Table 1, the symbol O indicates that it was fired excellently, the symbol Δ indicates that it was normally fired, and the symbol X indicates that no crystallization or flow occurred.

The glass samples 1 to 29 were heated in an electric furnace in the air to 1400 캜, melted for 1 hour and quenched to prepare glass. As a result, as shown in Table 1, among glass samples containing SiO ₂ -B ₂ O ₃ -Al ₂ O ₃ -ZnO-Na ₂ glasses, SiO ₂ was 10 to 20 mol% and B ₂ O ₃ , The content of Al ₂ O ₃ is from 0 to 5 mol%, the content of ZnO is from 15 to 35 mol%, the content of Na ₂ O is from 15 to 30 mol%, the molar ratio of SiO ₂ to Na ₂ O Is 0.4 to 1.1, and the molar ratio of SiO _{2 to} ZnO is 0.4 to 0.6. The glass sample is transparent.

Thereafter, each of the samples 1 to 29 was formed into powders of 100 μm or less to prepare glass frit, and the glasses of the samples 1 to 29 were heated to 550 ° C. and fired for 30 minutes. As shown in Table 1, as a result of firing, excellent firing results were mainly found in glass samples containing 10 to 20 mol% of SiO ₂ , and in other compositions, they were highly hygroscopic, crystallized after firing, or exhibited phase separation.

Of glass including a _{SiO 2 -B 2 O 3 -Al 2} O 3 -ZnO-Na 2 based glass according to the present invention the sample, SiO ₂ is from 10 to 20mol%, a B ₂ O ₃ is from 30 to 40mol% , and Al ₂ O ₃ is from 0 to 5mol%, ZnO 15 to 35 in mol%, Na ₂ O comprises 15 to 30 mol%, molar ratio of SiO ₂ to Na ₂ O is 0.4 to 1.1, The glass frit composition prepared from glass having a molar ratio of SiO ₂ to ZnO of 0.4 to 0.6 exhibited excellent firing results. In particular, a glass frit composition containing SiO ₂ in an amount of 10 to 20 mol% .

Accordingly, the glass composition for supporting a phosphor according to the present invention not only can be fired at a low temperature, but also exhibits excellent melting and firing results.

It will be apparent to those skilled in the art that various modifications, substitutions and substitutions are possible, without departing from the scope and spirit of the invention as disclosed in the accompanying claims. will be. Therefore, the embodiments disclosed in the present invention and the accompanying drawings are intended to illustrate and not to limit the technical spirit of the present invention, and the scope of the technical idea of the present invention is not limited by these embodiments and the accompanying drawings . The scope of protection of the present invention should be construed according to the following claims, and all technical ideas within the scope of equivalents should be construed as falling within the scope of the present invention.

10: Body
11: first lead
12: second lead
13: Side wall
14: wire
15:
21: Light emitting diode
30, 40, 50: wavelength converter
31, 41, 51: glass composition for supporting phosphor
32, 42, 52: Phosphor

Claims (7)

Comprising: a _{SiO 2 -B 2 O 3- Al 2} O 3 -ZnO-Na 2 O -based glass,
The SiO ₂ is from 10 to 20mol%, the B ₂ O ₃ is from 30 to 40mol%, the Al ₂ O ₃ is from 0 to 5mol%, the ZnO is 15 to 35mol%, the Na ₂ O from 15 to 30 mol%
The molar ratio of SiO ₂ to Na ₂ O is 0.4 to 1.1, the molar ratio of SiO _{2 to} ZnO is 0.4 to 0.6,
And a firing temperature of 550 DEG C or less. delete The method according to claim 1,
Further includes any one or a combination of any one selected from MgO, WO ₃ , SrO _, BaO, Al ₂ O _3, Y ₂ O ₃ , Ga ₂ O ₃ , In ₂ O ₃ , WO ₃ , GeO ₂ and La ₂ O ₃ Wherein the glass composition is a glass composition. The method according to claim 1,
R ₂ O,
Wherein the R is any one of Li, K, Rb and Cs, and the R ₂ O is 20 mol% or less. A glass composition for supporting a phosphor according to any one of claims 1 and 3 to 4; And
And a phosphor that is supported on the glass composition. The method of claim 5,
The phosphor may be at least one selected from the group consisting of a YAG-base phosphor, a TAG-base phosphor, a silicate-base phosphor, a Nitride base phosphor, a Fluoride base phosphor, an oxysulfide base phosphor, an oxynitride base phosphor , And an oxyfluoride-based phosphor, or a combination thereof. Light emitting diodes; And
And a wavelength converter for converting a wavelength of light emitted from the light emitting diode,
Wherein the wavelength converter comprises the glass composition for supporting a phosphor according to any one of claims 1 and 3 to 4; And
And a phosphor supported on the glass composition.

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