CN112159220B - 一种白光led/ld用高热稳定性高量子效率荧光陶瓷及其制备方法 - Google Patents
一种白光led/ld用高热稳定性高量子效率荧光陶瓷及其制备方法 Download PDFInfo
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Abstract
本发明公开了一种白光LED/LD用高热稳定性高量子效率荧光陶瓷及其制备方法,该荧光陶瓷化学式为:(Y y CezLu1‑z‑y)3(Sc x Al1‑x)2Al3O12,其中,x为Sc3+掺杂八面体Al3+位的摩尔百分数,y为Y3+掺杂Lu3+位的摩尔百分数,z为Ce3+掺杂Lu3+位的摩尔百分数,0.5<x≤0.8,0.4≤y≤0.6,y:x=2:3~3:4,0<z≤0.015,采用固相反应法烧结制得。本发明荧光陶瓷实现青绿光到绿黄光发射,色温4000~10000K,在150℃下发光强度衰减2%~5%,内量子效率在82%~88%之间。所制备陶瓷的工艺简单,易于工业化生产。
Description
技术领域
本发明涉及荧光陶瓷技术领域,具体涉及一种白光LED/LD用高热稳定性高量子效率荧光陶瓷及其制备方法。
背景技术
荧光转换型白光发光二极管和激光二极管(简称:LED/LD)作为新一代固态照明光源,因其发光效率高、鲁棒性好,器件体积小和使用寿命长等诸多优点,所以他们被广泛的关注和研究。随着技术的更新换代,将荧光粉Ce3+:Y3Al5O12 (简称:Ce:YAG)与有机硅胶混合的传统方式正逐步被激发源与Ce:YAG荧光陶瓷的远程激发封装方式所取代。作为颜色转化的核心材料,Ce:YAG荧光陶瓷以其导热系数高、机械性能好、物理和化学性能稳定,易实现高掺杂浓度等优点已经成为国内外研究的热点。然而,在蓝光LED/LD激发下,Ce:YAG荧光陶瓷具有明显的缺点,例如:发射出的光颜色比例失调、改良后的热猝灭温度低和量子效率低等缺点,从而导致制备的封装后器件的显色指数低、相对色温高和光效低等缺陷,难以满足高功率的使用要求。
目前已有文献报道对Ce:YAG荧光陶瓷进行发光行为和光谱发射峰的调节。但是,在进行调控发射光谱的性能时,荧光陶瓷的热稳定性和量子效率都会随之下降。量子效率会远小于原基质,在正常服役温度环境下,发光强度大都下降至 50%以下。目前国内外调控荧光陶瓷光谱的方法主要分为用Mg2+-Si4+离子对进行替换(J.Mater.Chem.C,2018,6,12200-12205.J.Mater.Chem.C,2016,4, 2359-2366.),添加红光离子(J.Eur.Ceram.Soc.,2017,37(10),3403–3409.),通过调控能级来增加发射光谱半高宽(ACSAppl.Mater.Interfaces,2019,11(2), 2130–2139.),复合结构实现红、绿、黄三色耦合发光(CN110218085A)。上述方法尽管能提高单个发光性能。但是,缺点也比较明显,生成纯石榴石相的加入外加离子的浓度很难精确控制,往往会产生杂相,那么相应荧光陶瓷的热稳定性和量子效率都有显著下降。
发明内容
本发明的目的之一是提供一种白光LED/LD用高热稳定性高量子效率荧光陶瓷,热稳定性高,量子效率高。
本发明的目的之二是提供上述白光LED/LD用高热稳定性量子效率荧光陶瓷的制备方法,易于工业化生产。
为实现上述目的,本发明采用的技术方案如下:一种白光LED/LD用高热稳定性高量子效率荧光陶瓷,该荧光陶瓷化学式为:
(YyCezLu1-z-y)3(ScxAl1-x)2Al3O12
其中x为Sc3+掺杂八面体Al3+位的摩尔百分数,y为Y3+掺杂Lu3+位的摩尔百分数,z为Ce3+掺杂Lu3+位的摩尔百分数,0.5<x≤0.8,0.4≤y≤0.6,y:x=2: 3~3:4,0<z≤0.015。
在高功率蓝光LED(350~500mA)或蓝光LD(2W~10W)激发下,实现青绿光到绿黄光发射,色温4000~10000K,且随着器件运行,发光强度随温度升高降低不明显,150℃时发光强度衰减2%~5%,热稳定性极好。陶瓷内量子效率在 82%~88%之间。
本发明还提供上述白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,采用固相反应法烧结,具体包括以下步骤:
(1)按照化学式(YyCezLu1-z-y)3(ScxAl1-x)2Al3O12,0.5<x≤0.8,0.4≤y≤0.6, y:x=2:3~3:4,0<z≤0.015,中各元素的化学计量比分别称取α-氧化铝、氧化钇、氧化镥、氧化钪和氧化铈作为原料粉体;将原料粉体、球磨介质按一定比例混合球磨,获得混合料浆;
(2)将步骤(1)得到的混合料浆置于干燥箱中干燥,再将干燥后的混合粉体过筛;
(3)将步骤(2)过筛后的粉体放入磨具中成型后再进行冷等静压成型,得到相对密度为51%~52%的素坯;
(4)将步骤(3)所得素坯置于真空炉中烧结,烧结温度1680℃~1750℃,保温时间6h~10h,烧结真空度不低于10-4Pa,得到荧光陶瓷;
(5)将步骤(4)真空烧结后的荧光陶瓷进行空气退火处理,退火温度 1000℃~1150℃,保温时间为20h~50h,得到相对密度为99.2%~99.9%的荧光陶瓷。
优选的,步骤(1)中,所述球料比为3.5~4.5:1,其所选用磨球直径为 0.5cm~2cm。
优选的,步骤(1)中,所述球磨转速为170r/min~190r/min,球磨时间为 25h~40h。
优选的,步骤(1)中,所述球磨介质是无水乙醇,原料粉体与球磨介质的质量体积比为2~3:1g/ml。
优选的,步骤(2)中,所述干燥时间为10h~15h,干燥温度为60℃~70℃。
优选的,步骤(2)中,所述过筛的筛网目数为50目~150目,过筛次数4~6 次。
优选的,步骤(4)中,真空烧结阶段的升温速率为0.25~0.5℃/分钟,烧结完毕后降温速率为2~4℃/分钟。
优选的,步骤(4)中,空气退火阶段的升温速率为0.25~0.5℃/分钟,降温速率为2~4℃/分钟。
与现有技术相比,本发明具有如下有益效果:
1.本发明提供的荧光陶瓷,基于Ce:LuAG,采用Sc3+离子取代八面体Al3+离子格位和Y3+离子取代十二面体Lu3+离子的思想,充分利用处于八面体格位的 Sc3+离子和Al3+离子形成的新的有效离子半径与处于十二面体格位Y3+离子和 Lu3+离子形成的新的有效离子半径的匹配效应。在调节***的微配位结构的基础上,提供***的结构刚性,进而提高Ce3+离子发光热稳定性,同时该陶瓷还具有较高的量子效率。引入的八面体格位的Sc3+离子和十二面体各位的Y3+离子能够提升Ce3+离子所处晶体场环境的配位复杂度,进而改变发射光谱的半高宽和峰的位置,实现发射光颜色的可调节。
2.本发明通过固相反应法结合真空烧结技术,通过控制化学配比,使Sc3+离子只占据八面体Al3+离子格位,Y3+离子只占据十二面体Lu3+离子格位。整个***的离子半径匹配合适,获得了石榴石纯相的荧光陶瓷。
3.本发明提供的荧光陶瓷可以有效地解决Ce:YAG荧光陶瓷中青绿光不足问题和在高Sc含量下制备镥铝石榴石纯相的问题,可有效提高LED/LD器件发光性能。在高功率蓝光LED(350~500mA)或蓝光LD(2W~10W)的激发下,发射光谱主峰520~550nm之间,半高宽在90~110nm之间,实现青绿光到绿黄光发射,色温4000~10000K。
4.本发明提供的荧光陶瓷在150℃下发光强度衰减2%~5%,内量子效率在 82%~88%之间。
附图说明
图1为本发明实施例1、2制得荧光陶瓷的实物图;
图2为本发明实施例1、2和对比例制得荧光陶瓷的XRD图;
图3为本发明实施例1制得荧光陶瓷表面SEM图;
图4为本发明实施例1制得荧光陶瓷在460nm波长激发下的发射光谱;
图5为本发明实施例1制得荧光陶瓷在460nm波长的蓝光LED芯片 (I=350mA)激发下的电致发光光谱;
图6为本发明实施例1制得荧光陶瓷随温度变化的发射光谱图;
图7为本发明实施例2制得荧光陶瓷在460nm波长激发下的发射光谱;
图8为本发明实施例2制得荧光陶瓷在460nm波长的蓝光LED芯片 (I=350mA)激发下的电致发光光谱;
图9为本发明实施例1、2和对比例制得荧光陶瓷的透过率图;
图10为本发明对比例制得荧光陶瓷的实物图;
图11为本发明对比例制得荧光陶瓷表面SEM图。
具体实施方式
下面结合附图和具体实施例对本发明作进一步详细说明。
以下实施例中使用的原料粉体均为市售商品,纯度均大于99.9%,所述α相氧化铝平均粒径150nm~200nm;所述氧化钇平均粒径10nm~50nm;所述氧化镥平均粒径10nm~50nm;所述氧化钪平均粒径1nm~50nm;所述氧化铈平均粒径1nm~50nm。
实施例1:制备化学式为(Lu0.596Y0.4Ce0.004)3(Al0.4Sc0.6)2Al3O12荧光陶瓷
(1)设定目标产物质量为60g,按照化学式(Lu0.594Y0.4Ce0.006)3(Al0.2Sc0.8)2Al3O12中各元素的化学计量比分别称取α-氧化铝(15.25g)、氧化钇(10.55g)、氧化镥 (27.73g)、氧化钪(6.40g)和氧化铈(0.16g)作为原料粉体;将原料粉体、120ml 无水乙醇混合,加入直径为0.5mm氧化铝球210g,在氧化铝球磨罐中进行球磨,球磨转速为170r/min,球磨时间为40h;
(2)将步骤(1)球磨后的混和浆料置于60℃鼓风干燥箱中干燥10h,干燥后的混合粉体过50目筛,过筛6遍。
(3)将步骤(2)煅烧后的粉体放入磨具中干压成型后再进行冷等静压成型,成型后素坯的相对密度为51%;
(4)将步骤(4)得到的陶瓷素坯放入真空炉中烧结,烧结温度为1680℃,保温时间为10h,升温速率为0.25℃/分钟,烧结完毕后降温速率为2℃/分钟;
(5)将步骤(5)得到的陶瓷放入马弗炉中空气退火,退火温度1000℃,保温时间为50h,升温速率为0.25℃/分钟,烧结完毕后降温速率为2℃/分钟;陶瓷相对密度为99.2%。
将烧结后的透明陶瓷进行双面抛光至陶瓷厚度为1.0mm,得到高热稳定性高量子效率荧光陶瓷,其实物为青黄色透明陶瓷,陶瓷底下的字清晰可见(如图1 中编号1)。
将本实施例中得到的(Lu0.596Y0.4Ce0.004)3(Al0.4Sc0.6)2Al3O12荧光陶瓷进行XRD 测试,结果如图2所示,表明:所制备的材料为纯石榴石相。
将本实施例中得到的(Lu0.596Y0.4Ce0.004)3(Al0.4Sc0.6)2Al3O12荧光陶瓷置于扫描电子显微镜下观测,结果如图3所示,可以看到陶瓷晶粒尺寸均一,没有杂相存在,与XRD测试结果一致。
本实施例中得到的(Lu0.596Y0.4Ce0.004)3(Al0.4Sc0.6)2Al3O12荧光陶瓷在460nm波长激发下,如图4所示,其发射光谱主峰为539nm,半高宽102nm。将该陶瓷在 460nm的蓝光LED芯片(I=350mA)激发下进行电致发光光谱测试,如图5所示,能够实现青绿光发射,色温10000K。
将本实施例得到的(Lu0.596Y0.4Ce0.004)3(Al0.4Sc0.6)2Al3O12荧光陶瓷进行随温度变化的发射光谱测试。结果如图6所示,表明:随着温度增加,陶瓷的发光强度逐渐降低,150℃时发光强度仅降低2.3%。内量子效率为88%。
将本实施例中得到的(Lu0.596Y0.4Ce0.004)3(Al0.4Sc0.6)2Al3O12荧光陶瓷进行透过率测试,结果如图9所示,表明:该荧光陶瓷透过率T=69.06%@800nm。
实施例2:制备化学式为(Lu0.385Y0.6Ce0.015)3(Al0.2Sc0.8)2Al3O12荧光陶瓷
(1)设定目标产物质量为60g,按照化学式(Lu0.385Y0.6Ce0.015)3(Al0.2Sc0.8)2Al3O12中各元素的化学计量比分别称取α-氧化铝(14.36g)、氧化钇(16.84g)、氧化镥(19.04g)、氧化钪(9.14g)和氧化铈(0.64g)作为原料粉体;将原料粉体、180ml 无水乙醇混合,加入直径为2mm氧化铝球270g,在氧化铝球磨罐中进行球磨,球磨转速为190r/min,球磨时间为25h;
(2)将步骤(1)球磨后的混和浆料置于70℃鼓风干燥箱中干燥10h,干燥后的混合粉体过150目筛,过筛4遍。
(3)将步骤(2)煅烧后的粉体放入磨具中干压成型后再进行冷等静压成型,成型后素坯的相对密度为52%;
(4)将步骤(4)得到的陶瓷素坯放入真空炉中烧结,烧结温度为1750℃,保温时间为6h,升温速率为0.5℃/分钟,烧结完毕后降温速率为4℃/分钟;
(5)将步骤(5)得到的陶瓷放入马弗炉中空气退火,退火温度1150℃,保温时间为20h,升温速率为0.5℃/分钟,烧结完毕后降温速率为4℃/分钟;陶瓷相对密度为99.9%。
将烧结后的透明陶瓷进行双面抛光至陶瓷厚度为1.0mm,得到高热稳定性高量子效率荧光陶瓷,其实物为青黄色透明陶瓷,陶瓷底下的字清晰可见(如图1 中编号2)。
将本实施例中得到的(Lu0.385Y0.6Ce0.015)3(Al0.2Sc0.8)2Al3O12荧光陶瓷进行XRD 测试,测试结果如图2所示,表明:所制备的材料为纯石榴石相。
将本实施例中得到的(Lu0.385Y0.6Ce0.015)3(Al0.2Sc0.8)2Al3O12荧光陶瓷在460nm 波长激发下的发射光谱图,如图7所示,其发射光谱主峰为546nm,半高宽110nm。将该陶瓷在460nm的蓝光LED芯片(I=350mA)激发下进行电致发光光谱测试,如图8所示,能够实现绿黄光发射,色温是4000K。
将本实施例得到的(Lu0.385Y0.6Ce0.015)3(Al0.2Sc0.8)2Al3O12荧光陶瓷进行随温度变化的发射光谱测试。结果表明:随着温度增加,陶瓷的发光强度逐渐降低,150℃时发光强度仅降低4.8%。内量子效率为82%。
将本实施例中得到的(Lu0.385Y0.6Ce0.015)3(Al0.2Sc0.8)2Al3O12荧光陶瓷进行透过率测试,结果如图9所示,表明:该荧光陶瓷透过率T=63.61%@800nm。
对比例:制备化学式为(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12荧光陶瓷
(1)设定目标产物质量为60g,按照化学式(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12中各元素的化学计量比分别称取α-氧化铝(14.07g)、氧化镥(41.07g)、氧化钪(4.75g)和氧化铈(0.11g)作为原料粉体;将原料粉体、150ml无水乙醇混合,加入直径为1.5mm氧化铝球240g,在氧化铝球磨罐中进行球磨,球磨转速为 185r/min,球磨时间为20h;
(2)将步骤(1)球磨后的混和浆料置于60℃鼓风干燥箱中干燥10h,干燥后的混合粉体过50目筛,过筛6遍;
(3)将步骤(2)煅烧后的粉体放入磨具中干压成型后再进行冷等静压成型,成型后素坯的相对密度为51.5%;
(4)将步骤(4)得到的陶瓷素坯放入真空炉中烧结,烧结温度为1700℃,保温时间为6h,升温速率为0.25℃/分钟,烧结完毕后降温速率为2℃/分钟;
(5)将步骤(5)得到的陶瓷放入马弗炉中空气退火,退火温度1050℃,保温时间为15h,升温速率为0.25℃/分钟,烧结完毕后降温速率为2℃/分钟;陶瓷相对密度为99.1%。
将烧结后的透明陶瓷进行双面抛光至陶瓷厚度为1.0mm,得到荧光陶瓷,其实物为青黄色透明陶瓷,陶瓷底下的字被覆盖(如图10所示)。
将本对比例中得到的(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12荧光陶瓷进行XRD测试,测试结果如图2所示,表明:所制备的材料为石榴石相和氧化钪相。
将本对比例中得到的(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12荧光陶瓷置于扫描电子显微镜下观测,结果如图11所示,可以看到存在明显的杂质相,陶瓷主相晶粒和杂质相共存。
本实施例中得到的(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12荧光陶瓷在460nm波长激发下,其发射光谱主峰为519nm,半高宽88.7nm。将该陶瓷在蓝光460nm的 LED芯片(I=350mA)激发下进行电致发光光谱测试,能够实现深青光发射,色温8400K。
将本对比例得到的(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12荧光陶瓷进行随温度变化的发射光谱测试。结果表明:随着温度增加,陶瓷的发光强度逐渐降低,150℃时发光强度降低21.4%。内量子效率为72%。
将本对比例中得到的(Lu0.997Ce0.003)3(Al0.5Sc0.5)2Al3O12荧光陶瓷进行透过率测试,如图9所示,结果表明:该荧光陶瓷透过率T=0.34%@800nm。
Claims (7)
1.一种白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,该荧光陶瓷化学式为:
(Y y CezLu1-z-y)3(Sc x Al1-x)2Al3O12
其中,x为Sc3+掺杂八面体Al3+位的摩尔百分数,y为Y3+掺杂Lu3+位的摩尔百分数,z为Ce3+掺杂Lu3+位的摩尔百分数,0.5<x≤0.8,0.4≤y≤0.6,y:x=2:3~3:4,0<z≤0.015;当环境温度为150℃时,所述荧光陶瓷的发光强度衰减2%~5%,内量子效率在82%~88%之间;
采用固相反应法烧结,具体包括以下步骤:
(1)按照化学式(Y y CezLu1-z-y)3(Sc x Al1-x)2Al3O12,0.5<x≤0.8,0.4≤y≤0.6,y:x=2:3~3:4,0<z≤0.015中各元素的化学计量比分别称取α-氧化铝、氧化钇、氧化镥、氧化钪和氧化铈作为原料粉体;将原料粉体、球磨介质混合球磨,获得混合料浆;
(2)将步骤(1)得到的混合料浆置于干燥箱中干燥,再将干燥后的混合粉体过筛;
(3)将步骤(2)过筛后的粉体放入磨具中成型后再进行冷等静压成型,得到相对密度为51%~52%的素坯;
(4)将步骤(3)所得素坯置于真空炉中烧结,烧结温度1680℃~1750℃,保温时间6h~10h,烧结真空度不低于10-4Pa,得到荧光陶瓷;
(5)将步骤(4)真空烧结后的荧光陶瓷进行空气退火处理,退火温度1000℃~1150℃,保温时间为20h~50h,得到相对密度为99.2%~99.9%的荧光陶瓷。
2.根据权利要求1所述的白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,步骤(1)中,所述球磨转速为170r/min~190r/min,球磨时间为25h~40h。
3.根据权利要求1所述的白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,步骤(1)中,所述球磨介质是无水乙醇,原料粉体的质量与球磨介质的体积比为1g:2~3mL。
4.根据权利要求1所述的白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,步骤(2)中,所述干燥时间为10h~15h,干燥温度为60℃~70℃。
5.根据权利要求1所述的白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,步骤(2)中,所述过筛的筛网目数为50目~150目,过筛次数为4~6次。
6.根据权利要求1所述的白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,步骤(4)中,真空烧结阶段的升温速率为0.25~0.5℃/分钟,烧结完毕后降温速率为2~4℃/分钟。
7.根据权利要求1所述的白光LED/LD用高热稳定性高量子效率荧光陶瓷的制备方法,其特征在于,步骤(5)中,空气退火阶段的升温速率为0.25~0.5℃/分钟,烧结完毕后降温速率为2~4℃/分钟。
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