本發明之波長轉換構件之特徵在於具有：玻璃，其以陽離子%計含有0.1～80%之P5+
、及1～90%之Sn2+
，且以陰離子%計含有0.1～70%之F-
＋Cl-
，並且β-OH值為1 mm-1
以下；及螢光體，其密封於玻璃中而成。以下，對如此限定玻璃中之各成分之含量的理由進行說明。再者，於無特殊說明之情形時，與以下各成分之含量相關之說明中，「%」意指「陽離子%」或「陰離子%」。 P5+
為玻璃骨架之構成成分。又，具有提高透光率之效果，尤其是提高紫外線區域附近之透光率之效果較高。尤其是，於高折射率之玻璃之情形時，容易獲得由P5+
所獲得之透光率提高之效果。又，亦具有抑制失透之效果或使降伏點降低之作用。P5+
之含量為0.1～80%，較佳為1～78%，更佳為5～76%，進而較佳為10～77%，特佳為20～75%。若P5+
之含量過少，則變得難以獲得上述效果。另一方面，若P5+
之含量過多，則Sn2+
之含量相對減少，從而折射率變得容易降低，並且耐候性容易降低。 Sn2+
為用於達成高折射率特性且提高化學耐久性或耐候性之必需成分。又，亦有使降伏點降低之效果。Sn2+
之含量為1～90%，較佳為5～87.5%，更佳為10～85%，進而較佳為15～82.5%，特佳為20～80%。若Sn2+
之含量過少，則變得難以獲得上述效果。另一方面，若Sn2+
之含量過多，則難以實現玻璃化，或耐失透性容易降低。 P5+
＋Sn2+
之含量較佳為50%以上，更佳為70.5%以上，進而較佳為75%以上，特佳為80%以上，最佳為85%以上。若P5+
＋Sn2+
之含量過少，則耐失透性或機械強度變得容易降低。再者，上限並無特別限定，P5+
＋Sn2+
之含量可為100%，但於含有其他成分之情形時，較佳為99.9%以下，更佳為99%以下，進而較佳為95%以下，特佳為90%以下。 於玻璃中，可進而含有以下成分作為陽離子成分。 B3+
、Zn2+
、Si4+
及Al3+
為玻璃骨架之構成成分，尤其是提高化學耐久性之效果較大。B3+
＋Zn2+
＋Si4+
＋Al3+
之含量較佳為0～50%，更佳為0～30%，進而較佳為0.1～25%，特佳為0.5～20%，最佳為0.75～15%。若B3+
＋Zn2+
＋Si4+
＋Al3+
之含量過多，則耐失透性變得容易降低。又，伴隨著熔融溫度之上升而Sn金屬等析出，透光率變得容易降低。又，降伏點容易上升。進而，難以獲得高折射率之玻璃。再者，就提高耐候性之觀點而言，較佳為含有0.1%以上之B3+
＋Zn2+
＋Si4+
＋Al3+
。再者，各成分之較佳之含量範圍如下所述。 B3+
為構成玻璃骨架之成分。又，具有提高耐候性之效果，尤其是抑制玻璃中之P5+
等成分選擇性地溶出至水中之效果較大。B3+
之含量較佳為0～50%，更佳為0.1～45%，進而較佳為0.5～40%。若B3+
之含量過多，則折射率或耐失透性變得容易降低。又，有透光率降低之傾向。 Zn2+
為作為熔劑發揮作用之成分。又，有如下效果，即提高耐候性，抑制玻璃成分溶出至研磨洗淨水等各種洗淨溶液中，或抑制高溫高濕狀態下之玻璃表面之變質。又，Zn2+
亦有使玻璃化穩定之效果。鑒於以上內容，Zn2+
之含量較佳為0～40%，更佳為0.1～30%，進而較佳為0.2～20%。若Zn2+
之含量過多，則透光率降低，或容易失透。 Si4+
亦為構成玻璃骨架之成分。又，有提高耐候性之效果，尤其是抑制玻璃中之P5+
等成分選擇性地溶出至水中之效果較大。Si4+
之含量較佳為0～20%，更佳為0.1～15%。若Si4+
之含量過多，則折射率降低，或降伏點容易變高。又，因未溶解產生之條紋或氣泡容易殘存於玻璃中。 Al3+
為能夠與Si4+
或B3+
一起構成玻璃骨架之成分。又，有提高耐候性之效果，尤其是抑制玻璃中之P5+
等成分選擇性地溶出至水中之效果較大。Al3+
之含量較佳為0～20%，更佳為0.1～15%。若Al3+
之含量過多，則變得容易失透。又，有透光率降低之傾向。進而，熔融溫度變高，因未溶解產生之條紋或氣泡容易殘存於玻璃中。 Mg2+
、Ca2+
、Sr2+
及Ba2+
(鹼土金屬離子)為作為熔劑發揮作用之成分。又，有如下效果，即提高耐候性，抑制玻璃成分溶出至研磨洗淨水等各種洗淨溶液中，或抑制高溫濕潤狀態下之玻璃表面之變質。又，為提高玻璃之硬度之成分。然而，若該等成分之含量過多，則有液相溫度上升(液相黏度降低)，從而於熔融或成形步驟中容易析出失透物之傾向。其結果變得難以量產化。再者，該等成分具有不使折射率大幅變動之特徵。鑒於以上內容，Mg2+
＋Ca2+
＋Sr2+
＋Ba2+
之含量較佳為0～10%，更佳為0～7.5%，進而較佳為0.1～5%，特佳為0.2～1.5%。 Li+
為於鹼金屬氧化物中使軟化點降低之效果最大之成分。又，藉由與B3+
、Si4+
或Al3+
置換，可提高折射率。然而，由於Li+
之分相性較強，故而若其含量過多，則有液相溫度上升而容易析出失透物，從而作業性降低之虞。又，Li+
容易使化學耐久性降低，亦容易使透光率降低。進而，若Li+
自玻璃溶出，則存在使螢光體之發光顯著降低之情形。因此，Li+
之含量較佳為0～10%，更佳為0～5%，進而較佳為0～1%，特佳為0～0.1%。 Na+
與Li+
同樣地具有使軟化點降低之效果。又，藉由與B3+
、Si4+
或Al3+
置換，可提高折射率。然而，若其含量過多，則有折射率大幅降低、或促進條紋之產生之傾向。又，液相溫度上升，而於玻璃中容易析出失透物。又，Na+
容易使化學耐久性降低，亦容易使透光率降低。進而，若Na+
自玻璃溶出，則存在使螢光體之發光顯著降低之情形。因此，Na+
之含量較佳為0～10%，更佳為0～5%，進而較佳為0～1%，特佳為0～0.1%。 K+
亦與Li+
同樣地具有使軟化點降低之效果。又，藉由與B3+
、Si4+
或Al3+
置換，可提高折射率。然而，若其含量過多，則有折射率大幅下降、或耐候性下降之傾向。又，液相溫度上升，從而於玻璃中容易析出失透物。又，若K+
自玻璃溶出，則存在使螢光體之發光顯著降低之情形。進而，K+
容易使化學耐久性降低，亦容易使透光率降低。因此，K2
O之含量較佳為0～10%，更佳為0～5%，進而較佳為0～1%，特佳為0～0.1%。 再者，Li+
＋Na+
＋K+
之含量較佳為0～10%，更佳為0～5%，進而較佳為0～1%，特佳為0～0.1%。若Li+
＋Na+
＋K+
之含量過多，則有變得容易失透、或化學耐久性亦降低之傾向。又，變得難以獲得所需之光學特性。 再者，亦可含有Cs+
作為鹼金屬成分。Cs+
具有使軟化點降低之效果。然而，若其含量過多，則有折射率大幅降低、或耐候性降低之傾向。又，液相溫度上升，從而容易析出失透物。因此，Cs+
之含量較佳為0～1%，更佳為0～0.5%，進而較佳為不含有。 La3+
及Gd3+
為幾乎不使透光率降低而提高折射率之成分。然而，若其含量過多，則耐失透性變得容易降低。因此，該等成分之含量分別較佳為0～10%，更佳為0.1～7.5%，進而較佳為1～5%。 Ta5+
、W6+
及Nb5+
具有幾乎不使透光率降低而提高折射率之效果。然而，若其含量過多，則耐失透性變得容易降低。因此，該等成分之含量分別較佳為0～10%，更佳為0.1～7.5%，進而較佳為1～5%。 Ti4+
為具有提高折射率之效果之成分。又，為對耐失透性之提高較為有效之成分。然而，若其含量過多，則有透光率下降之傾向。尤其是，於Fe成分以雜質之形式大量地包含於玻璃中之情形時(例如20 ppm以上)，有透光率顯著降低之傾向。又，反之則耐失透性變得容易降低。因此，Ti4+
之含量較佳為0～10%，更佳為0.1～7.5%，進而較佳為1～5%以下。 Y3+
、Yb3+
及Ge4+
具有幾乎不使透光率降低而提高折射率之效果。然而，若其含量過多，則耐失透性變得容易降低。因此，該等成分之含量分別較佳為0～10%，更佳為0.1～7.5%，進而較佳為1～5%。 Te4+
及Bi3+
為容易使透光率降低之成分，尤其是於氧濃度較低之熔融條件下進行黑化，透光率顯著降低。因此，Te4+
及Bi3+
之含量分別較佳為0～1%，更佳為不含有。 Zr4+
為用於提高化學耐久性或耐候性、且獲得高折射率之光學特性之成分。Zr4+
之含量較佳為0～5%，更佳為0～4%，進而較佳為0.1%～3%，特佳為0.2～2%。若Zr4+
之含量過多，則耐失透性變得容易降低，或熔融溫度上升導致透光率容易降低。 La3+
＋Gd3+
＋Ta5+
＋W6+
＋Nb5+
＋Ti4+
＋Y3+
＋Yb3+
＋Ge4+
之含量較佳為0～10%，更佳為0.1～7.5%，進而較佳為0.2～5%，最佳為0.3～2.5%。若La3+
＋Gd3+
＋Ta5+
＋W6+
＋Nb5+
＋Ti4+
＋Y3+
＋Yb3+
＋Ge4+
之含量過多，則耐失透性變得容易降低，或熔融溫度上升導致透光率容易降低。再者，為了獲得高折射率且耐候性優異之玻璃，較佳為含有0.1%以上之La3+
＋Gd3+
＋Ta5+
＋W6+
＋Nb5+
＋Ti4+
＋Y3+
＋Yb3+
＋Ge4+
。 Fe3+
、Ni2+
及Co2+
為使透光率降低之成分。因此，該等成分之含量分別較佳為0.1%以下，更佳為不含有。 又，由於Ce4+
、Pr3+
、Nd3+
、Eu3+
、Tb3+
及Er3+
等稀土類成分亦有使透光率降低之虞，故而該等成分之含量分別較佳為未達0.1%，更佳為不含有。 In3+
由於其失透傾向較強，故而較佳為不含有。 再者，就環境上之理由而言，較佳為不含有Pb2+
及As3+
。 本發明中之玻璃含有為鹵化物離子之F-
或Cl-
作為陰離子。F-
及Cl-
具有使降伏點降低之作用或提高透光率之效果。然而，若其含量過多，則熔融時之揮發性變高，容易產生條紋。又，變得容易失透。本發明中之玻璃中之F-
＋Cl-
之含量為0.1～70%，較佳為1～67.5%，更佳為5～65%，進而較佳為2～30%，特佳為10～60%。再者，作為用於導入F-
或Cl-
之原料，除SnF2
或SnCl2
外，可列舉La、Gd、Ta、W、Nb、Y、Yb、Ge、Mg、Ca、Sr或Ba之氟化物及氯化物。 作為鹵化物離子，除上述成分以外亦可含有Br-
等。作為鹵化物離子以外，通常含有氧離子(O2-
)。 本發明中所使用之玻璃之β-OH值為1 mm-1
以下，較佳為0.5 mm-1
以下，更佳為0.1 mm-1
以下，進而較佳為0.08 mm-1
以下，特佳為0.06 mm-1
以下，最佳為0.05 mm-1
以下。若β-OH值過大，則耐候性變得容易降低。其結果在長期使用波長轉換構件時，因經時變化而容易發生劣化。又，若β-OH值過大，則變得容易於玻璃中產生氣泡。若玻璃中包含氣泡，則因氣泡中所包含之氧，導致尤其是耐久性較低之量子點螢光體或氮化物螢光體容易經時劣化。又，因波長轉換構件中所包含之氣泡而產生過度之光散射，因此發光效率容易降低。β-OH值之下限並無特別限定，但實際為0.001 mm-1
以上，進而為0.002 mm-1
以上。 β-OH值係表示玻璃中所包含之水分量之指標且被定義為如下。 β-OH值＝log(T1/T2)/t(mm-1
) 此處，T1為3846 mm-1
之透過率(%)，T2為於2500～3500 mm-1
之範圍內所見之因O-H振動所產生之吸熱峰之透過率(%)，可藉由傅立葉轉換紅外線光譜法等進行測定。t為試樣之厚度(mm)。 玻璃之折射率(nd)較佳為1.6以上，更佳為1.65以上，進而較佳為1.7以上，特佳為1.72以上。若玻璃之折射率過小，則來自波長轉換構件之光之提取效率容易降低。又，有玻璃與螢光體之折射率差變大，兩者界面處之光散射損耗變大，導致發光強度降低之虞。再者，上限並無特別限定，但若折射率過高，則有玻璃化之穩定性降低之傾向，故而較佳為1.95以下，更佳為1.9以下。 玻璃之著色度λ70
較佳為未達500 nm，更佳為470 nm以下，進而較佳為460 nm以下。若著色度λ70
過大，則有近紫外區域～可見光區域中之透光率較差之傾向。結果照射至螢光體之激發光量降低，或難以自波長轉換構件獲得所需色調之出射光。 玻璃之降伏點較佳為300℃以下，更佳為280℃以下，進而較佳為260℃以下，特佳為250℃以下。藉由使玻璃之降伏點滿足上述範圍，能夠以相對較低之溫度之熱處理於玻璃中密封螢光體，可抑制螢光體之劣化。 玻璃之軟化溫度(TF)與結晶化溫度(Tc)之差較佳為30℃以上，更佳為40℃以上，進而較佳為50℃以上。若軟化溫度(TF)與結晶化溫度(Tc)之差過小，則於熱處理時容易析出結晶。結果有透光率降低、或密封性變得不充分(例如玻璃粉末之燒結變得不充分而難以獲得緻密之燒結體)之傾向。 玻璃於20～100℃下之熱膨脹係數較佳為80×10-7
～220×10-7
/℃，更佳為100×10-7
～210×10-7
/℃，進而較佳為120×10-7
～200×10-7
/℃。若熱膨脹係數過低或過高，則用以固定波長轉換構件之基材、或波長轉換構件與用以接著基材之接著材料之熱膨脹係數變得不匹配，從而變得容易於高溫下使用時產生龜裂。 玻璃之基於JOGIS之耐水性較佳為3級以上。根據該構成，成為即便長期使用亦難以因經時變化而發生劣化之波長轉換構件。 玻璃可按如下方式製造。首先，在以成為所需組成之方式調製原料後，於熔融爐中進行熔融。作為原料，可使用氧化物、碳酸鹽、硝酸鹽、磷酸鹽、鹵化合物(氟化物、氯化物、溴化物、碘化物、砹化物)等。此處，在藉由一次熔融製作玻璃屑後，使用該玻璃屑進行二次熔融，藉此可實現折射率之調整或組成之均質化。熔融氣氛較佳為設為惰性氣氛或還原性氣氛。例如藉由於氮氣或氬氣等惰性氣氛中進行熔融，而容易獲得均質之玻璃。作為玻璃熔融用容器，可使用鉑或金等金屬、耐火物、石英玻璃、氧化鋁、玻璃石墨等。尤其是金製容器由於難以與Sn2+
發生合金反應，故而較佳。再者，作為金屬製容器，較佳為使用分散有ZrO2
等氧化物之補強材料。 再者，可藉由熔融條件調整玻璃中之β-OH值。具體而言，熔融溫度越高、且熔融時間越長，則β-OH值越容易降低。熔融時間及熔融溫度之較佳範圍雖亦根據組成而有所不同，但例如熔融溫度較佳為400～1000℃，更佳為450～800℃，進而較佳為500～700℃，特佳為520～600℃。又，熔融時間較佳為0.5～50小時，更佳為0.6～10小時，進而較佳為0.8～5小時。若熔融溫度過低、或熔融時間過短，則β-OH值容易變高。另一方面，若熔融溫度過高、或熔融時間過長，則Sn金屬等析出，導致透光率變得容易降低。又，陰離子成分等揮發，而容易產生無法獲得所需之組成、或產生條紋等不良情況。 熔融玻璃可流出至模具而成形為板狀，亦可流出至一對冷卻輥間而成形為膜狀。於獲得玻璃粉末之情形時，將成形為板狀或膜狀之玻璃利用球磨機等進行粉碎。 玻璃粉末之粒徑並無特別限定，例如較佳為：最大粒徑D99
為200 μm以下(尤其是150 μm以下，進而105 μm以下)，且平均粒徑D50
為0.1 μm以上(尤其是1 μm以上，進而2 μm以上)。若玻璃粉末之最大粒徑D99
過大，則於波長轉換構件中，激發光變得難以散射，從而發光效率容易降低。又，若平均粒徑D50
過小，則於波長轉換構件中，激發光過度散射，從而發光效率容易降低。再者，平均粒徑D50
及最大粒徑D99
係指藉由雷射繞射法所測得之值。 作為螢光體，一般只要為市場中可取得者則並無特別限定。例如可列舉氮化物螢光體、氮氧化物螢光體、氧化物螢光體(包含YAG螢光體等石榴石系螢光體)、硫化物螢光體、氧硫化物螢光體、鹵化物螢光體(鹵磷酸氯化物螢光體等)、鋁酸鹽螢光體及量子點螢光體等。該等螢光體通常為粉末狀。該等螢光體中，氮化物螢光體、氮氧化物螢光體及氧化物螢光體由於耐熱性較高，於焙燒時相對難以劣化，故而較佳。再者，氮化物螢光體及氮氧化物螢光體具有如下特徵：將近紫外～藍色之激發光轉換成綠色～紅色這種範圍寬廣之波長區域，並且發光強度亦相對較高。因此，氮化物螢光體及氮氧化物螢光體尤其作為白色LED元件用波長轉換構件所用之螢光體較為有效。 作為上述螢光體，可列舉於波長300～500 nm具有激發帶且於波長380～780 nm具有發光波峰者，尤其是發出藍色(波長440～480 nm)、綠色(波長500～540 nm)、黃色(波長540～595 nm)或紅色(波長600～700 nm)光者。 作為當照射波長300～440 nm之紫外～近紫外之激發光時發出藍色光之螢光體，可列舉：(Sr，Ba)MgAl10
O17
：Eu2+
、(Sr，Ba)3
MgSi2
O8
：Eu2+
等。 作為當照射波長300～440 nm之紫外～近紫外之激發光時發出綠色螢光的螢光體，可列舉：SrAl2
O4
：Eu2+
、SrBaSiO4
：Eu2+
、Y3
(Al，Gd)5
O12
：Ce3+
、SrSiOn
：Eu2+
、BaMgAl10
O17
：Eu2+
，Mn2+
、Ba2
MgSi2
O7
：Eu2+
、Ba2
SiO4
：Eu2+
、Ba2
Li2
Si2
O7
：Eu2+
、BaAl2
O4
：Eu2+
等。 作為當照射波長440～480 nm之藍色之激發光時發出綠色螢光的螢光體，可列舉：SrAl2
O4
：Eu2+
、SrBaSiO4
：Eu2+
、Y3
(Al，Gd)5
O12
：Ce3+
、SrSiOn：Eu2+
、β-SiAlON：Eu2+
等。 作為當照射波長300～440 nm之紫外～近紫外之激發光時發出黃色螢光的螢光體，可列舉La3
Si6
N11
：Ce3+
等。 作為當照射波長440～480 nm之藍色之激發光時發出黃色螢光的螢光體，可列舉：Y3
(Al，Gd)5
O12
：Ce3+
、Sr2
SiO4
：Eu2+
。 作為當照射波長300～440 nm之紫外～近紫外之激發光時發出紅色螢光的螢光體，可列舉：CaGa2
S4
：Mn2+
、MgSr3
Si2
O8
：Eu2+
，Mn2+
、Ca2
MgSi2
O7
：Eu2+
，Mn2+
等。 作為當照射波長440～480 nm之藍色之激發光時發出紅色螢光的螢光體，可列舉：CaAlSiN3
：Eu2+
、CaSiN3
：Eu2+
、(Ca，Sr)2
Si5
N8
：Eu2+
、α-SiAlON：Eu2+
等。 作為量子點螢光體之具體例，可列舉：CdSe、CdTe、ZnSe、CdS、PbSe、PbS、CIS、ZCIS、ZCIGS、CdSe/ZnS、ZnS/CdSe/ZnS、CdSe/ZnSe/ZnS等。量子點螢光體通常於使之分散於有機溶劑中之狀態下處理。 再者，亦可根據激發光或發光之波長區域而混合使用複數個螢光體。例如，於照射紫外區域之激發光而獲得白色光之情形時，只要混合使用發出藍色、綠色、黃色、紅色之螢光的螢光體即可。 若波長轉換構件中之螢光體之含量過多，則產生激發光變得難以被效率良好地照射至螢光體、或機械強度容易降低等之問題。另一方面，若螢光體之含量過少，則難以獲得所需之發光強度。就此種觀點而言，波長轉換構件中之螢光體之含量以質量%計，較佳為於0.01～50%、更佳為0.05～40%、進而較佳為0.1～30%之範圍內進行調整。 再者，於旨在使波長轉換構件中產生之螢光反射至激發光入射側而主要僅將螢光提取至外部之波長轉換構件中，可增多螢光體之含量(例如以質量%計為50%～80%，進而為55～75%)以使發光強度達到最大，而不限定於上述內容。 本發明之波長轉換構件只要為於玻璃中密封螢光體而成者則無特別限定。例如可列舉包含玻璃粉末與螢光體粉末之燒結體者。又，可列舉於複數片(例如2片)玻璃板間夾持螢光體而成者。於該情形時，複數片玻璃板較佳為於周緣部相互熔合，抑或由玻璃料等密封材料密封。 玻璃粉末與螢光體粉末之燒結體可藉由輥壓成形進行製作。具體而言，在將玻璃粉末與螢光體粉末混合而獲得混合粉末後，將該混合粉末投入至一對加熱輥間隙。為了提高機械強度等，混合粉末中亦可混合無機填料。混合粉末一面藉由輥進行加熱壓製，一面於輥之旋轉方向被擠出。藉此，混合粉末被成形為片狀。根據該成形方法，加熱時間較短，故而可抑制螢光體之熱劣化。又，藉由使混合粉末通過加熱輥間，而玻璃粉末在軟化之同時被壓碎，就該方面而言容易獲得緻密之片狀波長轉換構件。再者，就於使用量子點螢光體作為螢光體之情形時，由於螢光體粒子尺寸較小，故而螢光體粒子相對於輥之接觸電阻變小，就該方面而言成形性容易提高。又，就玻璃粉末與螢光體粒子之間之接觸電阻亦變小之方面而言，玻璃粉末彼此之密接性(燒結性)容易提高。 輥之間隙大小可根據目標片材之厚度適當設定。輥之轉速可根據混合粉末之種類、或輥之溫度等適當設定。 成形步驟例如可於空氣、氮氣或氬氣之氣氛下進行。就抑制玻璃粉末或螢光體之特性劣化之觀點而言，較佳為於氮氣、氬氣等惰性氣體中進行成形。又，成形亦可於減壓氣氛下進行。藉由於減壓氣氛下進行成形，可抑制氣泡殘存於波長轉換構件中。 本發明之發光裝置之特徵在於具備：上述波長轉換構件、及對波長轉換構件照射螢光體之激發光之光源。圖1係表示本發明之發光裝置之一實施形態的示意性側視圖。如圖1所示，發光裝置1係具備波長轉換構件2及光源3而成。光源3係對波長轉換構件2照射螢光體之激發光Lin
。入射至波長轉換構件2之激發光Lin
被轉換成其他波長之光，自與光源3相反側以Lout
之形式射出。此時，可使波長轉換後之光與未經波長轉換而透過之激發光之合成光射出，亦可僅使波長轉換後之光射出。 [實施例] 以下，基於實施例對本發明進行詳細說明，但本發明並不限於該等實施例。 (1)玻璃之製作 表1分別表示本發明之實施例及比較例之玻璃。 [表1]
首先，以成為表1所示之各玻璃組成之方式調製原料，使用石英燒杯於表1所記載之條件下進行熔融。在將所獲得之熔融玻璃流出至一對冷卻輥間而成形為膜狀後，藉由利用球磨機進行粉碎而獲得平均粒徑10 μm之玻璃粉末。又，將熔融玻璃之一部分澆鑄至碳模框中，藉此製作適合各測定之板狀試樣。 針對所獲得之試樣，對β-OH值、折射率(nd)、熱膨脹係數、降伏點、耐候性進行測定或評價。將結果示於表1。 β-OH值係使用傅立葉轉換紅外線分光計(珀金埃爾默公司製造，商品名FT-IR Frontier)進行測定。測定時使用15 mm×15 mm×1 mm之經雙面光學研磨之試樣。 折射率係以針對氦燈之d射線(587.6 nm)之測定值進行表示。 熱膨脹係數及降伏點係使用熱膨脹測定裝置(dilato meter)進行測定。再者，熱膨脹係數係於20～100℃之溫度範圍內測定。 耐候性按如下方式進行評價。將經光學研磨之試樣於高溫高濕槽(愛斯佩克公司製造，商品名：SH-221)中在85℃、相對濕度85%之條件下保持20小時。目視觀察保持後之試樣表面之狀態，將未確認出風化者評價為「◎」，將雖稍微確認有風化但實用上沒有問題者評價為「○」，將清晰地確認出風化者評價為「×」。自表1可知，試樣a、b之耐候性相對良好，但試樣c之耐候性較差。 (2)波長轉換構件之製作 表2表示實施例(No.1、2)及比較例(No.3)。 [表2]
對表1所記載之各玻璃粉末試樣，滴加以成為表2所示之特定比率之方式分散有作為螢光體之CdSe/ZnS之溶劑(己烷)並進行混合，進而藉由於真空氣氛下保持而使溶劑揮發。藉此獲得包含玻璃粉末與螢光體粉末之混合粉末。將混合粉末利用模具進行加壓成型而製作直徑1 cm之圓柱狀壓粉體。於將該壓粉體夾持於一對玻璃板間之狀態下，在氮氣氣氛中以150℃～200℃熱壓接壓製60秒，而獲得燒結體。對所獲得之燒結體實施加工，藉此獲得7 mm×2 mm×0.4 mm之短條狀之波長轉換構件。對於所獲得之波長轉換構件測定發光光譜，算出發光效率。將結果示於表2。 發光效率按如下方式算出。首先，於激發波長460 nm之LED光源上覆蓋開有1 mm之孔之鋁製遮罩，於孔上設置波長轉換構件，於積分球內測定自試樣上表面發出之光之能量分佈光譜。其次，用所獲得之光譜乘以標準比視感度計算總光通量，用總光通量除以光源之電力算出發光效率。 自表2可知，實施例1～2之波長轉換構件雖發光效率優異，為0.1～0.22(lm)，但比較例3之波長轉換構件未檢測出螢光，發光效率為0(lm)。 [產業上之可利用性] 本發明之波長轉換構件作為顯示器、普通照明、特殊照明(例如投影器光源、車輛用前照燈光源)等所使用之單色或白色LED等之構成構件較佳。The wavelength conversion member of the present invention is characterized by having glass, which contains 0.1 to 80% of P 5+ as a cationic%, and Sn 2+ of 1 to 90%, and 0.1 to 70% of F as an anionic%. - + Cl - and a β-OH value of 1 mm -1 or less; and a phosphor formed by sealing in glass. The reason for limiting the content of each component in the glass in this way will be described below. In addition, in the case where there is no special explanation, in the description related to the content of each component below, "%" means "cationic%" or "anionic%". P 5+ is a constituent of the glass skeleton. In addition, it has the effect of increasing the light transmittance, especially the effect of increasing the light transmittance near the ultraviolet region. In particular, in the case of a glass having a high refractive index, it is easy to obtain the effect of improving the light transmittance obtained by P 5+ . It also has the effect of suppressing devitrification or reducing the yield point. The content of P 5+ is 0.1 to 80%, preferably 1 to 78%, more preferably 5 to 76%, still more preferably 10 to 77%, and particularly preferably 20 to 75%. When the content of P 5+ is too small, it becomes difficult to obtain the above effects. On the other hand, when the content of P 5+ is too large, the content of Sn 2+ is relatively reduced, so that the refractive index is easily reduced, and the weather resistance is easily reduced. Sn 2+ is an essential component for achieving high refractive index characteristics and improving chemical durability or weather resistance. It also has the effect of lowering the drop point. The content of Sn 2+ is 1 to 90%, preferably 5 to 87.5%, more preferably 10 to 85%, still more preferably 15 to 82.5%, and particularly preferably 20 to 80%. When the content of Sn 2+ is too small, it becomes difficult to obtain the above effects. On the other hand, if the content of Sn 2+ is too large, it becomes difficult to achieve vitrification or the devitrification resistance is liable to decrease. The content of P 5+ + Sn 2+ is preferably 50% or more, more preferably 70.5% or more, still more preferably 75% or more, particularly preferably 80% or more, and most preferably 85% or more. When the content of P 5+ + Sn 2+ is too small, devitrification resistance or mechanical strength tends to decrease. In addition, the upper limit is not particularly limited, and the content of P 5+ + Sn 2+ may be 100%, but when other components are contained, it is preferably 99.9% or less, more preferably 99% or less, and even more preferably 95 % Or less, particularly preferably 90% or less. The glass may further contain the following components as a cationic component. B 3+ , Zn 2+ , Si 4+ and Al 3+ are the constituent components of the glass skeleton, and especially the effect of improving the chemical durability is great. The content of B 3+ + Zn 2+ + Si 4+ + Al 3+ is preferably 0 to 50%, more preferably 0 to 30%, still more preferably 0.1 to 25%, particularly preferably 0.5 to 20%, and most preferably 0.75 to 15%. When the content of B 3+ + Zn 2+ + Si 4+ + Al 3+ is too large, devitrification resistance tends to decrease. In addition, as the melting temperature increases, Sn metal or the like is precipitated, and the light transmittance tends to decrease. Moreover, the fall point is likely to rise. Furthermore, it is difficult to obtain a glass having a high refractive index. Furthermore, from the viewpoint of improving weather resistance, it is preferable to contain B 3+ + Zn 2+ + Si 4+ + Al 3+ in an amount of 0.1% or more. In addition, the preferable content range of each component is as follows. B 3+ is a component constituting a glass skeleton. In addition, it has the effect of improving weather resistance, and particularly has the effect of inhibiting the selective elution of components such as P 5+ in glass into water. The content of B 3+ is preferably 0 to 50%, more preferably 0.1 to 45%, and still more preferably 0.5 to 40%. When the content of B 3+ is too large, the refractive index or devitrification resistance tends to decrease. In addition, the transmittance tends to decrease. Zn 2+ is a component that functions as a flux. In addition, it has the effects of improving the weather resistance, suppressing the elution of glass components into various cleaning solutions such as grinding and washing water, or suppressing the deterioration of the glass surface under high temperature and high humidity conditions. In addition, Zn 2+ also has the effect of stabilizing glass transition. In view of the above, the content of Zn 2+ is preferably 0 to 40%, more preferably 0.1 to 30%, and still more preferably 0.2 to 20%. When the content of Zn 2+ is too large, the light transmittance is reduced, or devitrification is liable to occur. Si 4+ is also a component constituting the glass skeleton. In addition, it has the effect of improving the weather resistance, and in particular, the effect of inhibiting the selective dissolution of components such as P 5+ in the glass into water. The content of Si 4+ is preferably 0 to 20%, and more preferably 0.1 to 15%. When the content of Si 4+ is too large, the refractive index decreases or the yield point tends to increase. In addition, streaks or bubbles due to undissolution tend to remain in the glass. Al 3+ is a component capable of forming a glass skeleton together with Si 4+ or B 3+ . In addition, it has the effect of improving the weather resistance, and in particular, the effect of inhibiting the selective dissolution of components such as P 5+ in the glass into water. The content of Al 3+ is preferably 0 to 20%, and more preferably 0.1 to 15%. When the content of Al 3+ is too large, devitrification becomes easy. In addition, the transmittance tends to decrease. Furthermore, the melting temperature becomes higher, and streaks or bubbles due to undissolution tend to remain in the glass. Mg 2+ , Ca 2+ , Sr 2+, and Ba 2+ (alkaline earth metal ions) are components that function as fluxes. In addition, it has the effects of improving the weather resistance, suppressing the elution of glass components into various cleaning solutions such as grinding and washing water, or suppressing the deterioration of the glass surface under high temperature and wet conditions. In addition, it is a component for improving the hardness of glass. However, when the content of these components is too large, the liquidus temperature rises (the liquidus viscosity decreases), and devitrification tends to be easily precipitated during the melting or forming step. As a result, it becomes difficult to mass-produce. In addition, these components have a feature that they do not greatly change the refractive index. In view of the above, the content of Mg 2+ + Ca 2+ + Sr 2+ + Ba 2+ is preferably 0 to 10%, more preferably 0 to 7.5%, still more preferably 0.1 to 5%, and particularly preferably 0.2 to 1.5%. . Li + is a component that has the greatest effect of reducing the softening point among alkali metal oxides. Further, by replacing with B 3+ , Si 4+ or Al 3+ , the refractive index can be increased. However, since Li + has a strong phase separation property, if the content thereof is too large, devitrified substances are likely to be precipitated due to an increase in the liquidus temperature and workability may be reduced. In addition, Li + is liable to reduce chemical durability and also to reduce light transmittance. Furthermore, when Li + is eluted from the glass, the luminescence of the phosphor may be significantly reduced. Therefore, the content of Li + is preferably 0 to 10%, more preferably 0 to 5%, still more preferably 0 to 1%, and particularly preferably 0 to 0.1%. Na + and Li + in the same manner having the effect of reducing the softening point. Further, by replacing with B 3+ , Si 4+ or Al 3+ , the refractive index can be increased. However, if the content is too large, the refractive index tends to be greatly reduced, or the generation of streaks tends to be promoted. In addition, the liquidus temperature rises, and devitrified substances are easily precipitated in the glass. In addition, Na + is liable to reduce chemical durability and also to reduce light transmittance. Furthermore, when Na + is eluted from glass, the luminescence of a fluorescent body may fall significantly. Therefore, the content of Na + is preferably 0 to 10%, more preferably 0 to 5%, still more preferably 0 to 1%, and particularly preferably 0 to 0.1%. K + also has the effect of lowering the softening point similarly to Li + . Further, by replacing with B 3+ , Si 4+ or Al 3+ , the refractive index can be increased. However, if the content is too large, the refractive index tends to decrease significantly, or the weather resistance tends to decrease. In addition, as the liquidus temperature rises, devitrified substances are easily precipitated in the glass. In addition, when K + is eluted from the glass, the luminescence of the phosphor may be significantly reduced. Furthermore, K + is liable to decrease the chemical durability and also to decrease the light transmittance. Therefore, the content of K 2 O is preferably 0 to 10%, more preferably 0 to 5%, still more preferably 0 to 1%, and particularly preferably 0 to 0.1%. The content of Li + + Na + + K + is preferably 0 to 10%, more preferably 0 to 5%, still more preferably 0 to 1%, and particularly preferably 0 to 0.1%. When the content of Li + + Na + + K + is too large, devitrification tends to occur, or chemical durability tends to decrease. In addition, it becomes difficult to obtain desired optical characteristics. Furthermore, Cs + may be contained as an alkali metal component. Cs + has the effect of reducing the softening point. However, if the content is too large, there is a tendency that the refractive index significantly decreases or the weather resistance decreases. In addition, the liquidus temperature rises, so that devitrified substances are easily precipitated. Therefore, the content of Cs + is preferably 0 to 1%, more preferably 0 to 0.5%, and even more preferably not contained. La 3+ and Gd 3+ are components that increase the refractive index with little reduction in light transmittance. However, if the content is too large, devitrification resistance tends to decrease. Therefore, the contents of these components are preferably 0 to 10%, more preferably 0.1 to 7.5%, and even more preferably 1 to 5%. Ta 5+ , W 6+ and Nb 5+ have the effect of increasing the refractive index with little reduction in light transmittance. However, if the content is too large, devitrification resistance tends to decrease. Therefore, the contents of these components are preferably 0 to 10%, more preferably 0.1 to 7.5%, and even more preferably 1 to 5%. Ti 4+ is a component having an effect of increasing the refractive index. In addition, it is a component that is more effective in improving devitrification resistance. However, if the content is too large, the transmittance tends to decrease. In particular, when the Fe component is contained in the glass in a large amount as an impurity (for example, 20 ppm or more), the transmittance tends to be significantly reduced. On the other hand, devitrification resistance tends to decrease. Therefore, the content of Ti 4+ is preferably 0 to 10%, more preferably 0.1 to 7.5%, and still more preferably 1 to 5%. Y 3+ , Yb 3+, and Ge 4+ have the effect of increasing the refractive index while hardly reducing the transmittance. However, if the content is too large, devitrification resistance tends to decrease. Therefore, the contents of these components are preferably 0 to 10%, more preferably 0.1 to 7.5%, and even more preferably 1 to 5%. Te 4+ and Bi 3+ are components that are liable to decrease the light transmittance, and are particularly blackened under a melting condition where the oxygen concentration is low, and the light transmittance is significantly reduced. Therefore, the contents of Te 4+ and Bi 3+ are preferably 0 to 1%, and more preferably they are not contained. Zr 4+ is a component for improving chemical durability or weather resistance and obtaining optical characteristics with a high refractive index. The content of Zr 4+ is preferably 0 to 5%, more preferably 0 to 4%, still more preferably 0.1% to 3%, and particularly preferably 0.2 to 2%. When the content of Zr 4+ is too large, the devitrification resistance tends to be lowered, or the transmittance is easily lowered due to an increase in the melting temperature. The content of La 3+ ＋ Gd 3+ ＋ Ta 5+ ＋ W 6+ ＋ Nb 5+ ＋ Ti 4+ ＋ Y 3+ ＋ Yb 3+ ＋ Ge 4+ is preferably 0 to 10%, more preferably 0.1 to 7.5%, and even more preferably 0.2. ~ 5%, most preferably 0.3 ~ 2.5%. When the content of La 3+ ＋ Gd 3+ ＋ Ta 5+ ＋ W 6+ ＋ Nb 5+ ＋ Ti 4+ ＋ Y 3+ ＋ Yb 3+ ＋ Ge 4+ is too much, the devitrification resistance becomes easy to decrease, or the light transmittance is caused by the increase in melting temperature. Easy to lower. Furthermore, in order to obtain a glass having a high refractive index and excellent weather resistance, it is preferable to contain La 3+ + Gd 3+ + Ta 5+ + W 6+ + Nb 5+ + Ti 4+ + Y 3+ + Yb 3+ + Ge 4+ . Fe 3+ , Ni 2+ and Co 2+ are components that reduce the light transmittance. Therefore, the contents of these components are each preferably 0.1% or less, and more preferably not contained. In addition, since rare earth components such as Ce 4+ , Pr 3+ , Nd 3+ , Eu 3+ , Tb 3+, and Er 3+ may also reduce the light transmittance, the contents of these components are preferably as follows: It is less than 0.1%, and more preferably does not contain it. In 3+ has a strong devitrification tendency, so it is preferably not contained. Furthermore, for environmental reasons, it is preferable not to contain Pb 2+ and As 3+ . The glass in the present invention contains F - or Cl - which is a halide ion as an anion. F - and Cl - have the effect of lowering the drop point or increasing the light transmittance. However, if the content is too large, the volatility at the time of melting becomes high, and streaks tend to occur. Moreover, it becomes easy to devitrify. In the present invention, the glass in the F - + Cl - content of 0.1 to 70%, preferably from 1 to 67.5%, more preferably 5 to 65%, and further preferably from 2 to 30%, particularly preferably 10 to 60 %. Further, as for introducing F - or Cl - raw materials, in addition to outer 2 SnF 2 or SnCl2, include La, Gd, Ta, W, Nb, Y, Yb, Ge, Mg, Ca, Sr or Ba of fluorine Compounds and chlorides. As the halide ion, Br - and the like may be contained in addition to the above components. In addition to the halide ion, an oxygen ion (O 2- ) is usually contained. The β-OH value of the glass used in the present invention is 1 mm -1 or less, preferably 0.5 mm -1 or less, more preferably 0.1 mm -1 or less, even more preferably 0.08 mm -1 or less, particularly preferably 0.06 mm -1 or less, preferably 0.05 mm -1 or less. If the β-OH value is too large, the weather resistance tends to decrease. As a result, when the wavelength conversion member is used for a long period of time, deterioration easily occurs due to changes with time. When the β-OH value is too large, it becomes easy to generate bubbles in the glass. If bubbles are contained in the glass, the quantum dot phosphors or nitride phosphors, which have particularly low durability, are liable to deteriorate over time due to the oxygen contained in the bubbles. In addition, since excessive light scattering occurs due to bubbles contained in the wavelength conversion member, the light emission efficiency is liable to decrease. The lower limit of the β-OH value is not particularly limited, but it is actually 0.001 mm -1 or more, and further 0.002 mm -1 or more. The β-OH value is an index representing the amount of water contained in glass and is defined as follows. β-OH value = log (T1 / T2) / t (mm -1 ) Here, T1 is the transmittance (%) of 3846 mm -1 and T2 is the factor OH seen in the range of 2500 ～ 3500 mm -1 The transmittance (%) of the endothermic peak generated by vibration can be measured by Fourier transform infrared spectroscopy and the like. t is the thickness (mm) of the sample. The refractive index (nd) of the glass is preferably 1.6 or more, more preferably 1.65 or more, even more preferably 1.7 or more, and particularly preferably 1.72 or more. If the refractive index of the glass is too small, the extraction efficiency of light from the wavelength conversion member tends to decrease. In addition, there is a possibility that the refractive index difference between the glass and the phosphor becomes larger, and the light scattering loss at the interface between the two becomes larger, resulting in a decrease in luminous intensity. The upper limit is not particularly limited, but if the refractive index is too high, the stability of glass transition tends to decrease. Therefore, it is preferably 1.95 or less, and more preferably 1.9 or less. The chromaticity λ 70 of the glass is preferably less than 500 nm, more preferably 470 nm or less, and even more preferably 460 nm or less. If the degree of coloring λ 70 is too large, the transmittance in the near-ultraviolet region to the visible light region tends to be poor. As a result, the amount of excitation light irradiated to the phosphor is reduced, or it is difficult to obtain the emitted light of a desired hue from the wavelength conversion member. The fall point of glass is preferably 300 ° C or lower, more preferably 280 ° C or lower, even more preferably 260 ° C or lower, and particularly preferably 250 ° C or lower. By making the drop point of the glass satisfy the above range, the phosphor can be sealed in the glass at a relatively low temperature heat treatment, and the deterioration of the phosphor can be suppressed. The difference between the softening temperature (TF) and the crystallization temperature (Tc) of the glass is preferably 30 ° C or higher, more preferably 40 ° C or higher, and even more preferably 50 ° C or higher. If the difference between the softening temperature (TF) and the crystallization temperature (Tc) is too small, crystals tend to precipitate during heat treatment. As a result, there is a tendency that the light transmittance is reduced or the sealing properties become insufficient (for example, the sintering of glass powder becomes insufficient and it is difficult to obtain a dense sintered body). The thermal expansion coefficient of glass at 20 to 100 ° C is preferably 80 × 10 -7 to 220 × 10 -7 / ° C, more preferably 100 × 10 -7 to 210 × 10 -7 / ° C, and further preferably 120 × 10 -7 to 200 × 10 -7 / ℃. If the coefficient of thermal expansion is too low or too high, the substrate used to fix the wavelength conversion member, or the coefficient of thermal expansion of the wavelength conversion member and the material used to adhere to the substrate will not match, making it easier to use it at high temperatures. Cracks occur. The JOGIS-based water resistance of glass is preferably level 3 or higher. According to this configuration, it becomes a wavelength conversion member that is hardly deteriorated by a change with time even if it is used for a long time. The glass can be manufactured as follows. First, after preparing a raw material so that it may become a desired composition, it melts in a melting furnace. As raw materials, oxides, carbonates, nitrates, phosphates, halogen compounds (fluoride, chloride, bromide, iodide, halide), and the like can be used. Here, after the glass flakes are produced by primary melting, the glass flakes are used for secondary melting, whereby the adjustment of the refractive index or the homogenization of the composition can be achieved. The melting atmosphere is preferably an inert atmosphere or a reducing atmosphere. For example, homogeneous glass is easily obtained by melting in an inert atmosphere such as nitrogen or argon. As the glass melting container, metals such as platinum or gold, refractories, quartz glass, alumina, and glass graphite can be used. In particular, a gold container is preferred because it is difficult to cause an alloy reaction with Sn 2+ . As the metal container, it is preferable to use a reinforcing material in which an oxide such as ZrO 2 is dispersed. Moreover, the β-OH value in the glass can be adjusted by the melting conditions. Specifically, the higher the melting temperature and the longer the melting time, the easier the β-OH value decreases. Although the preferable ranges of the melting time and the melting temperature also vary depending on the composition, for example, the melting temperature is preferably 400 to 1000 ° C, more preferably 450 to 800 ° C, and still more preferably 500 to 700 ° C. 520 ～ 600 ℃. The melting time is preferably 0.5 to 50 hours, more preferably 0.6 to 10 hours, and still more preferably 0.8 to 5 hours. If the melting temperature is too low or the melting time is too short, the β-OH value tends to increase. On the other hand, if the melting temperature is too high or the melting time is too long, Sn metal or the like will be precipitated and the light transmittance will tend to decrease. In addition, anionic components and the like are volatilized, and problems such as failure to obtain a desired composition or occurrence of streaks tend to occur. The molten glass may flow out into a mold and be formed into a plate shape, or it may flow out between a pair of cooling rolls and be formed into a film shape. When a glass powder is obtained, the glass formed into a plate shape or a film shape is pulverized by a ball mill or the like. The particle diameter of the glass powder is not particularly limited. For example, it is preferable that the maximum particle diameter D 99 is 200 μm or less (especially 150 μm or less, and then 105 μm or less), and the average particle diameter D 50 is 0.1 μm or more (especially 1 μm or more, and further 2 μm or more). If the maximum particle diameter D 99 of the glass powder is too large, it is difficult to scatter the excitation light in the wavelength conversion member, and the light emission efficiency is liable to decrease. When the average particle diameter D 50 is too small, the excitation light is excessively scattered in the wavelength conversion member, so that the luminous efficiency is liable to decrease. In addition, the average particle diameter D 50 and the maximum particle diameter D 99 are values measured by a laser diffraction method. The phosphor is not particularly limited as long as it is available in the market. Examples include nitride phosphors, oxynitride phosphors, oxide phosphors (including garnet phosphors such as YAG phosphors), sulfide phosphors, oxysulfide phosphors, and halogenated phosphors. Material phosphors (halophosphate chloride phosphors, etc.), aluminate phosphors, quantum dot phosphors, etc. These phosphors are usually powdered. Among these phosphors, nitride phosphors, oxynitride phosphors, and oxide phosphors are preferable because they have high heat resistance and are relatively difficult to deteriorate during firing. In addition, nitride phosphors and oxynitride phosphors have the following characteristics: they convert excitation light from near ultraviolet to blue into a wide wavelength region such as green to red, and their luminous intensity is relatively high. Therefore, nitride phosphors and oxynitride phosphors are particularly effective as phosphors for wavelength conversion members for white LED elements. Examples of the phosphor include those having an excitation band at a wavelength of 300 to 500 nm and an emission peak at a wavelength of 380 to 780 nm, and particularly emitting blue (wavelength 440 to 480 nm) and green (wavelength 500 to 540 nm). , Yellow (wavelength 540 to 595 nm) or red (wavelength 600 to 700 nm) light. Examples of phosphors that emit blue light when irradiated with ultraviolet to near-ultraviolet excitation light at a wavelength of 300 to 440 nm include (Sr, Ba) MgAl 10 O 17 : Eu 2+ , (Sr, Ba) 3 MgSi 2 O 8 : Eu 2+ and the like. Examples of phosphors that emit green fluorescence when irradiated with ultraviolet to near-ultraviolet excitation light having a wavelength of 300 to 440 nm include SrAl 2 O 4 : Eu 2+ , SrBaSiO 4 : Eu 2+ , and Y 3 (Al, Gd) 5 O 12 : Ce 3+ , SrSiO n : Eu 2+ , BaMgAl 10 O 17 : Eu 2+ , Mn 2+ , Ba 2 MgSi 2 O 7 : Eu 2+ , Ba 2 SiO 4 : Eu 2+ , Ba 2 Li 2 Si 2 O 7 : Eu 2+ , BaAl 2 O 4 : Eu 2+ and the like. Examples of phosphors that emit green fluorescence when irradiated with blue excitation light having a wavelength of 440 to 480 nm include SrAl 2 O 4 : Eu 2+ , SrBaSiO 4 : Eu 2+ , and Y 3 (Al, Gd). 5 O 12 : Ce 3+ , SrSiOn: Eu 2+ , β-SiAlON: Eu 2+ and the like. Examples of the phosphor that emits yellow fluorescence when irradiated with ultraviolet to near-ultraviolet excitation light having a wavelength of 300 to 440 nm include La 3 Si 6 N 11 : Ce 3+ and the like. Examples of the phosphor that emits yellow fluorescence when irradiated with blue excitation light having a wavelength of 440 to 480 nm include: Y 3 (Al, Gd) 5 O 12 : Ce 3+ , Sr 2 SiO 4 : Eu 2+ . Examples of the phosphor that emits red fluorescence when irradiated with ultraviolet to near-ultraviolet excitation light with a wavelength of 300 to 440 nm include CaGa 2 S 4 : Mn 2+ , MgSr 3 Si 2 O 8 : Eu 2+ , Mn 2+ , Ca 2 MgSi 2 O 7 : Eu 2+ , Mn 2+ and the like. Examples of the phosphor that emits red fluorescence when irradiated with blue excitation light having a wavelength of 440 to 480 nm include CaAlSiN 3 : Eu 2+ , CaSiN 3 : Eu 2+ , (Ca, Sr) 2 Si 5 N 8 : Eu 2+ , α-SiAlON: Eu 2+, and the like. Specific examples of the quantum dot phosphor include CdSe, CdTe, ZnSe, CdS, PbSe, PbS, CIS, ZCIS, ZCIGS, CdSe / ZnS, ZnS / CdSe / ZnS, CdSe / ZnSe / ZnS, and the like. The quantum dot phosphor is usually processed in a state of being dispersed in an organic solvent. Furthermore, a plurality of phosphors may be mixed and used according to the wavelength region of the excitation light or light emission. For example, in the case where white light is obtained by irradiating the excitation light in the ultraviolet region, it is sufficient to use a phosphor that emits blue, green, yellow, and red fluorescence. If the content of the phosphor in the wavelength conversion member is too large, problems such as that it becomes difficult for the excitation light to be efficiently irradiated to the phosphor, or the mechanical strength is easily reduced, and the like are caused. On the other hand, if the content of the phosphor is too small, it may be difficult to obtain a desired luminous intensity. From such a viewpoint, the content of the phosphor in the wavelength conversion member is measured in mass%, preferably in a range of 0.01 to 50%, more preferably 0.05 to 40%, and still more preferably 0.1 to 30%. Adjustment. Furthermore, in a wavelength conversion member that is designed to reflect the fluorescent light generated in the wavelength conversion member to the incident side of the excitation light and mainly only extracts the fluorescent light to the outside, the content of the phosphor can be increased (for example, as mass% is 50% to 80%, and further 55 to 75%) to maximize the light emission intensity, and is not limited to the above. The wavelength conversion member of the present invention is not particularly limited as long as the phosphor is sealed in glass. For example, a sintered body containing a glass powder and a phosphor powder is mentioned. Moreover, the thing which clamped the fluorescent substance among several (for example, two) glass plates is mentioned. In this case, the plurality of glass plates are preferably fused to each other at the peripheral portion, or are sealed with a sealing material such as glass frit. Sintered bodies of glass powder and phosphor powder can be produced by roll forming. Specifically, after the glass powder and the phosphor powder are mixed to obtain a mixed powder, the mixed powder is put into a gap between a pair of heating rollers. In order to improve mechanical strength and the like, an inorganic filler may be mixed in the mixed powder. The mixed powder is extruded in the direction of rotation of the roller while being heated and pressed by the roller. Thereby, the mixed powder is shaped into a sheet shape. According to this molding method, since the heating time is short, thermal degradation of the phosphor can be suppressed. In addition, by passing the mixed powder between the heating rollers and crushing the glass powder while softening, it is easy to obtain a dense sheet-shaped wavelength conversion member in this respect. Furthermore, in the case of using a quantum dot phosphor as the phosphor, since the size of the phosphor particles is small, the contact resistance of the phosphor particles with respect to the roller becomes small, and formability is easy in this respect improve. Moreover, since the contact resistance between a glass powder and a fluorescent particle also becomes small, the adhesiveness (sinterability) of glass powder with each other is easy to improve. The gap size of the roller can be appropriately set according to the thickness of the target sheet. The rotation speed of the roller can be appropriately set according to the type of the mixed powder or the temperature of the roller. The forming step can be performed in an atmosphere of air, nitrogen, or argon, for example. From the viewpoint of suppressing deterioration of the characteristics of the glass powder or the phosphor, it is preferable to perform the molding in an inert gas such as nitrogen or argon. The molding may be performed under a reduced pressure atmosphere. By molding under a reduced pressure atmosphere, it is possible to suppress bubbles from remaining in the wavelength conversion member. The light-emitting device of the present invention includes the above-mentioned wavelength conversion member and a light source that irradiates the wavelength conversion member with excitation light of a phosphor. FIG. 1 is a schematic side view showing an embodiment of a light emitting device according to the present invention. As shown in FIG. 1, the light emitting device 1 includes a wavelength conversion member 2 and a light source 3. 3 based on excitation light source 2 is irradiated phosphor light of the wavelength conversion member L in. Is incident to the excitation light wavelength conversion member 2 is converted into L in light of other wavelengths, emitted from the side opposite to the light source 3 in the form of L out. In this case, the combined light of the wavelength-converted light and the excitation light transmitted without the wavelength conversion may be emitted, or only the light after the wavelength conversion may be emitted. [Examples] Hereinafter, the present invention will be described in detail based on examples, but the present invention is not limited to these examples. (1) Production of glass Table 1 shows the glass of Examples and Comparative Examples of the present invention, respectively. [Table 1] First, a raw material was prepared so that it might become each glass composition shown in Table 1, and it melt | fused using the quartz beaker on the conditions described in Table 1. After the obtained molten glass was flowed out between a pair of cooling rolls and formed into a film shape, it was pulverized by a ball mill to obtain a glass powder having an average particle diameter of 10 μm. In addition, a part of the molten glass was cast into a carbon mold frame, thereby preparing a plate-like sample suitable for each measurement. The obtained sample was measured or evaluated for β-OH value, refractive index (nd), thermal expansion coefficient, drop point, and weather resistance. The results are shown in Table 1. The β-OH value was measured using a Fourier transform infrared spectrometer (manufactured by PerkinElmer, trade name FT-IR Frontier). A 15 mm × 15 mm × 1 mm specimen with double-sided optical grinding was used for the measurement. The refractive index is expressed by a measurement value of d-ray (587.6 nm) of a helium lamp. The thermal expansion coefficient and drop point are measured using a thermal expansion measuring device (dilato meter). The thermal expansion coefficient is measured in a temperature range of 20 to 100 ° C. The weather resistance was evaluated as follows. The optically polished sample was kept in a high-temperature and high-humidity tank (manufactured by Espek Corporation, trade name: SH-221) for 20 hours at 85 ° C and 85% relative humidity. Visually observe the state of the surface of the sample after the retention, evaluate those who have not confirmed weathering as "◎", those who have slightly confirmed weathering but have no practical problems as "○", and those who clearly confirm weathering are rated as " × ". As can be seen from Table 1, the weather resistance of samples a and b is relatively good, but the weather resistance of sample c is poor. (2) Preparation of wavelength conversion member Table 2 shows examples (No. 1, 2) and comparative examples (No. 3). [Table 2] For each glass powder sample described in Table 1, a solvent (hexane) in which CdSe / ZnS as a phosphor was dispersed was added dropwise so as to have a specific ratio shown in Table 2, and mixed, and further, under a vacuum atmosphere, Keep and let the solvent evaporate. Thereby, a mixed powder including a glass powder and a phosphor powder is obtained. The mixed powder was press-molded with a mold to produce a cylindrical compact powder having a diameter of 1 cm. The pressed powder was sandwiched between a pair of glass plates, and was thermally press-bonded at 150 ° C. to 200 ° C. for 60 seconds in a nitrogen atmosphere to obtain a sintered body. The obtained sintered body was processed to obtain a short strip-shaped wavelength conversion member of 7 mm × 2 mm × 0.4 mm. The light emission spectrum was measured about the obtained wavelength conversion member, and the light emission efficiency was calculated. The results are shown in Table 2. The luminous efficiency was calculated as follows. First, the LED light source with an excitation wavelength of 460 nm is covered with An aluminum mask with a 1 mm hole is provided with a wavelength conversion member on the hole, and the energy distribution spectrum of the light emitted from the upper surface of the sample is measured in the integrating sphere. Second, multiply the obtained spectrum by the standard specific sensitivity to calculate the total luminous flux, and divide the total luminous flux by the power of the light source to calculate the luminous efficiency. As can be seen from Table 2, although the wavelength conversion members of Examples 1 to 2 had excellent luminous efficiency of 0.1 to 0.22 (lm), the wavelength conversion member of Comparative Example 3 did not detect fluorescence, and the luminous efficiency was 0 (lm). [Industrial Applicability] The wavelength conversion member of the present invention is preferably used as a constituent member of a monochromatic or white LED used in a display, general lighting, special lighting (for example, a light source for a projector, a light source for a vehicle headlight, etc.) .