Lutetium nitride-based phosphor and light emitting device comprising same

Abstract

A lutetium nitride-based phosphor and a light emitting device comprising the same, wherein the lutetium nitride-based phosphor comprises an inorganic compound, and the composition of the inorganic compound comprises at least an M element, an A element, a D element and an R element; the M element is one or two elements selected from a group consisting of Lu, La, Pr, Nd, Sm, Y, Tb and Gd, and necessarily comprises Lu; the A element is Si and/or Ge; the D element is one or two elements selected from a group consisting of O, N and F, and necessarily comprises N; the R element is Ce and/or Dy, and the atomic molar ratio of the Lu element in the M element is greater than 50%. Because the ion radius of Lu3+ is smaller than the ion radius of La3+, the light color performance thereof can be flexibly adjusted according to needs.

Claims

1. A lutetium nitride-based phosphor, comprising an inorganic compound, wherein the composition of the inorganic compound comprises at least an M element, an A element, a D element and an R element, wherein the M element is one or two elements selected from a group consisting of Lu, La, Pr, Nd, Sm, Y, Tb and Gd, and necessarily comprises Lu; the A element is Si and/or Ge; the D element is one or two elements selected from a group consisting of O, N and F, and necessarily comprises N; the R element is Ce and/or Dy, and the atomic molar ratio of the Lu element in the M element is greater than 50%, wherein the inorganic compound has a crystal structure the same as Y.sub.3Si.sub.6N.sub.11; the inorganic compound has a composition of M.sub.3-aA.sub.xD.sub.y:aR, wherein parameters a, x and y satisfy the following conditions: 0<a≤0.8, 5≤x≤7, 10≤y≤12.

2. The lutetium nitride-based phosphor according to claim 1, wherein the atomic molar ratio of the Lu element in the M element is ≥70%, preferably ≥80%.

3. The lutetium nitride-based phosphor according to claim 1, wherein the A element is Si.

4. The lutetium nitride-based phosphor according to claim 1, wherein the D element is N.

5. The lutetium nitride-based phosphor according to claim 1, wherein the R element is Ce.

6. The lutetium nitride-based phosphor according to claim 5, wherein 0.1≤a≤0.5; 5.5≤x≤6.5, preferably x=6; 10.5≤y≤11.5, preferably y=11.

7. The lutetium nitride-based phosphor according to claim 1, wherein the lutetium nitride-based phosphor has a peak wavelength of excitation spectrum at 400 to 460 nm, and can emit a peak wavelength covering the range between 475 to 540 nm.

8. A light emitting device, comprising a fluorescent substance and an excitation light source, wherein the fluorescent substance comprises the lutetium nitride-based phosphor according to claim 1.

9. The light emitting device according to claim 8, wherein the excitation light source is a semiconductor light emitting diode or a laser light source, preferably, the excitation light source has an emission peak wavelength of 400 to 490 nm.

10. The light emitting device according to claim 8, wherein the fluorescent substance further comprises another/other phosphor(s) selected from a group consisting of anyone or more of (Y,Gd,Lu,Tb).sub.3(Al,Ga).sub.5O.sub.12:Ce.sup.3+,β-SiAlON:Eu.sup.2+, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+, (Li,Na,K).sub.2(Ti,Zr,Si,Ge)F.sub.6:Mn.sup.4+ and (Ca,Sr,Ba)MgAl.sub.10O.sub.17:Eu.sup.2+.

11. The lutetium nitride-based phosphor according to claim 1, wherein the A element is Si, the D element is N, and the R element is Ce.

12. The lutetium nitride-based phosphor according to claim 1, wherein the A element is Si, the D element is N, and the R element is Ce, and 0.1≤a≤0.5; 5.5≤x≤6.5, preferably x=6; 10.5≤y≤11.5, preferably y=11.

13. The lutetium nitride-based phosphor according to claim 1, wherein the A element is Si, the D element is N, and the R element is Ce, 0.1≤a≤0.5; 5.5≤x≤6.5, preferably x=6; 10.5≤y≤111.5, preferably y=11; the lutetium nitride-based phosphor has a peak wavelength of excitation spectrum at 400 to 460 nm, and can emit a peak wavelength covering the range between 475 to 540 nm.

14. The light emitting device according to claim 8, wherein the excitation light source is a semiconductor light emitting diode or a laser light source, preferably, the excitation light source has an emission peak wavelength of 400 to 490 nm; and the fluorescent substance further comprises another/other phosphor(s) selected from a group consisting of anyone or more of (Y,Gd,Lu,Tb).sub.3(Al,Ga).sub.5O.sub.12:Ce.sup.3+,β-SiAlON:Eu.sup.2+, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+, (Li,Na,K).sub.2(Ti,Zr,Si,Ge)F.sub.6:Mn.sup.4+ and (Ca,Sr,Ba)MgAl.sub.10O.sub.17:Eu.sup.2+.

15. The light emitting device according to claim 8, wherein the excitation light source is a semiconductor light emitting diode or a laser light source, preferably, the excitation light source has an emission peak wavelength of 400 to 490 nm; the fluorescent substance further comprises another/other phosphor(s) selected from a group consisting of anyone or more of (Y,Gd,Lu,Tb).sub.3(Al,Ga).sub.5O.sub.12:Ce.sup.3+,β-SiAlON:Eu.sup.2+, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+, (Li,Na,K).sub.2(Ti,Zr,Si,Ge)F.sub.6:Mn.sup.4+ and (Ca,Sr,Ba)MgAl.sub.10O.sub.17:Eu.sup.2+; and the A element is Si, the D element is N, and the R element is Ce.

16. The light emitting device according to claim 8, wherein the excitation light source is a semiconductor light emitting diode or a laser light source, preferably, the excitation light source has an emission peak wavelength of 400 to 490 nm; the fluorescent substance further comprises another/other phosphor(s) selected from a group consisting of anyone or more of (Y,Gd,Lu,Tb).sub.3(Al,Ga).sub.5O.sub.12:Ce.sup.3+,β-SiAlON:Eu.sup.2+, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+, (Li,Na,K).sub.2(Ti,Zr,Si,Ge)F.sub.6:Mn.sup.4+ and (Ca,Sr,Ba)MgAl.sub.10O.sub.17:Eu.sup.2+; the A element is Si, the D element is N, and the R element is Ce; and 0.1≤a≤0.5; 5.5≤x≤6.5, preferably x=6; 10.5≤y≤11.5, preferably y=11.

17. The light emitting device according to claim 8, wherein the excitation light source is a semiconductor light emitting diode or a laser light source, preferably, the excitation light source has an emission peak wavelength of 400 to 490 nm; the fluorescent substance further comprises another/other phosphor(s) selected from a group consisting of anyone or more of (Y,Gd,Lu,Tb).sub.3(Al,Ga).sub.5O.sub.12:Ce.sup.3+, β-SiAlON:Eu.sup.2+, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+, (Li,Na,K).sub.2(Ti,Zr,Si,Ge)F.sub.6:Mn.sup.4+ and (Ca,Sr,Ba)MgAl.sub.10O.sub.17:Eu.sup.2+; the A element is Si, the D element is N, and the R element is Ce; 0.1≤a≤0.5; 5.5≤x≤6.5, preferably x=6; 10.5≤y≤11.5, preferably y=11; and the lutetium nitride-based phosphor has a peak wavelength of excitation spectrum at 400 to 460 nm, and can emit a peak wavelength covering the range between 475 to 540 nm.

Description

EXPLANATIONS OF THE ACCOMPANYING DRAWINGS

(1) The drawings accompanying the Description that constitutes a part of the present application is used to provide further comprehension of the present invention. The exemplary examples of the present invention and the explanations thereof are meant to explain the present invention, but should not be so construed as to restrict the present invention. In the drawings:

(2) FIG. 1 illustrates XRD diffraction patterns of the lutetium nitride-based phosphor according to Example 1 of the present invention;

(3) FIG. 2 illustrates excitation spectrum and emission spectrum of the lutetium nitride-based phosphor according to Example 1 of the present invention; and

(4) FIG. 3 is a diagram of a light emitting device of the present application.

SPECIFIC EXAMPLES

(5) As should be noted, under the circumstance of not being conflictive, examples and features in the Examples of the present application can be mutually combined. The present invention will be described in detail below in conjunction with the Examples.

(6) As has been noted in the Background Art, although currently available nitride phosphor is rather good in terms of thermal stability, its emission spectrum is difficultly adjustable, so it is hard to flexibly adjust its photochromic property according to needs, and this in turn restricts its application. In order to address the above problem, the present application provides a phosphor, and a light emitting device having the phosphor.

(7) In a typical example of the present application there is provided a lutetium nitride-based phosphor comprising an inorganic compound; the composition of the inorganic compound comprises at least an M element, an A element, a D element and an R element, of which the M element is one or two elements selected from a group consisting of Lu, La, Pr, Nd, Sm, Y, Tb and Gd, and necessarily comprises Lu; the A element is Si and/or Ge; the D element is one or two elements selected from a group consisting of O, N and F, and necessarily comprises N; the R element is Ce and/or Dy, and the atomic molar ratio of the Lu element in the M element is greater than 50%.

(8) The inorganic compound is used as a constituent part of the phosphor or used as the phosphor per se, so based on comprising the above elements its composition has the crystal structure suitable for forming a phosphor, or it can be understood thus that the aforementioned elements are utilized to substitute corresponding elements of the inorganic compound forming the existing phosphor—for instance, the M element is used to substitute a corresponding lanthanide element. The following theoretic explanation is made all on the basis of having the crystal structure of a phosphor. Since the ion radius of Lu.sup.3+ is smaller than that of La.sup.3+, when the inorganic compound forming the phosphor comprises the Lu element, the original ligand site would be contracted; in order to reduce lattice distortion due to the ligand site contraction, the adjacent ligand site expands, and this weakens the existing crystal field environment, so that the emission spectrum of the lutetium nitride-based phosphor having the inorganic compound can be easily adjusted,—even adjusted to the green light region, and therefore its photochromic property can be flexibly adjusted according to needs; at the same time, since the content of the Lu element is greater than 50%, the main component of the inorganic compound is changed, that is to say, the originally substituted element is changed to the Lu element, and such change ameliorates lattice distortion and forms single crystal grains of relatively uniform formations the single crystal grains have long-range order, i.e., the inorganic compound achieves better crystallization properties; furthermore, its thermal stability is relatively good to the extent that the need for high-density energy excitation can be satisfied.

(9) Out of the above theoretical consideration, preferably, the inorganic compound has a crystal structure the same as Y.sub.3Si.sub.6N.sub.11. The inorganic compound according to the present application differs in structure from the existing La.sub.3Si.sub.6N.sub.11:Ce.sup.3+, but it retains the generality of excellent thermal stability with commercially available La.sub.3Si.sub.6N.sub.11:Ce.sup.3+ phosphor, and the emission efficiency of the claimed inorganic compound has more room for improvement than La.sub.3Si.sub.6N.sub.11:Ce.sup.3+— for instance, the emission spectrum of this inorganic compound is more flexibly adjustable.

(10) In a preferred example of the present application, the inorganic compound preferably has a composition of M.sub.3-aA.sub.xD.sub.y:aR, wherein parameters a, x and y satisfy the following conditions: 0<a≤0.8, 5≤x≤7, 10≤y≤12.

(11) In the above composition, big quantities of Lu substitute the La element, and after Lu has substituted La to a certain degree, the crystal structure is changed into Y.sub.3Si.sub.6N.sub.11, with the adjustable range of the emission spectrum more broader the emission spectrum can be adjusted from 475 nm to 540 nm; moreover, compared with Y.sub.3Si.sub.6N.sub.11:Ce.sup.3+, the emission strength and thermal stability of the lutetium nitride-based phosphor according to the present application are apparently enhanced, while thermal stability is basically consistent with that of La.sub.3Si.sub.6N.sub.11:Ce.sup.3+, so based on retaining the excellent thermal stability of La.sub.3Si.sub.6N.sub.11:Ce.sup.3+, the present application enables the preparation of a lutetium nitride-based phosphor that is higher in emission efficiency than Y.sub.3Si.sub.6N.sub.11:Ce.sup.3+, and more flexible in spectrum adjustability than La.sub.3Si.sub.6N.sub.11:Ce.sup.3+.

(12) Lu is the main medium material of the inorganic compound in the present application, and there is a certain atomic number proportional relationship between the activator and the M element in the medium material in order to guarantee that the phosphor obtained after doping of the activator has higher emission efficiency, it is preferable that the atomic molar ratio of the Lu element in the M element is 70%, preferably 80%.

(13) In another preferred example of the present application, the A element is Si. It is further preferred that the D element is N. It is more preferred that the R element is Ce. Since the difference between ion radii Lu.sup.3+ (0.848 Å) and Ce.sup.3+ (1.03 Å) is greater than the difference between ion radii La.sup.3+ (1.06 Å) and Ce.sup.3+ (1.03 Å), after the aforementioned inorganic compound has been doped with small amount of Ce.sup.3+, lattice distortion is partially strengthened due to the relatively great difference between Ce and Lu ion radii, thereby leading to increase in the crystal field strength, and, at the same time, there are two types of Lu lattice sites with relatively great difference in partial ligand site environments in the inorganic compound. On the basis of the above two points, 5d energy level splitting of Ce.sup.3+ is enhanced, whereby the adjustability flexibility of the emission spectrum of the inorganic compound is further enhanced.

(14) As has been found after test and research, when the content of the R element is too few, since the luminescence center is few, the brightness would be low; when the content of the R element is too high, concentration quenching would occur thereby leading to enhancement of non-radiative transition, so brightness would also be low, so 0.1≤a≤0.5 is preferred; in order to obtain a white LED device having pure phase, excellent crystallization property, consistence in single crystal grains and forms, high emission efficiency and high color rendering index, the range is preferably 5.5≤x≤6.5, more preferably x=6; 10.5≤y≤11.5, more preferably y=11.

(15) The lutetium nitride-based phosphor with thus composed inorganic compound has a peak wavelength of excitation spectrum at 400 to 460 nm—a range broader than the emission spectrum of existing nitride phosphors, and more easily adjustable—and emits a peak wavelength covering the range between 475 to 540 nm, that is to say, it can emit blue-bluish green-green-bluish green lights.

(16) The aforementioned phosphor of the present application can be prepared by the method in the patent document recited in the Background Art section, and preferably prepared by the following steps:

(17) step 1) proportioning materials according to chemical formula M.sub.3-aA.sub.xD.sub.y:aR, selecting a simple substance, a nitride, an oxide selected from an element M, an element A, an element D and an element R or an alloy thereof, and taking and uniformly mixing the source materials according to molar ratios required by the above chemical formula to obtain a mixture;
step 2) placing the mixture obtained by step 1) into a container and calcinating the same in nitrogen or other non-oxidizing conditions to obtain a calcinated product, wherein the highest sintering temperature is from 1500 to 2000° C., and the holding time is 5 to 20 hours; and
step 3)—sequentially subjecting the calcinated product in step 2) to crushing, washing, sieving and baking processes to obtain the phosphor.

(18) In another typical example of the present application, there is provided a light emitting device comprising a fluorescent substance and an excitation light source, of which the fluorescent substance comprises the aforementioned lutetium nitride-based phosphor. Since the lutetium nitride-based phosphor according to the present application has high thermal stability and easy adjustability of emission spectrum, the light emitting device having the phosphor has high operating stability and longer use life, and is applicable to many different requirements.

(19) In a preferred example of the present application, the excitation light source is a semiconductor light emitting diode or a laser light source, preferably, the excitation light source has an emission peak wavelength of 400 to 490 nm. Excitation bands of currently commercially available LED excitation light sources lie within the range, specifically, there are two types of excitation light sources: near ultraviolet diode with the wavelength range between 380 to 420 nm, and blue diode with the wavelength range between 420 to 490 nm. Moreover, the excitation peak wavelength of the aforementioned phosphor is about 440 nm, so the use of a light emitting diode within the above wavelength range facilitates photoluminescence of the phosphor.

(20) In order to further improve the emission effect of the light emitting device, it is preferred that the fluorescent substance further comprises other phosphors selected from the group consisting of anyone or more of (Y,Gd,Lu,Tb).sub.3(Al,Ga).sub.5O.sub.12:Ce.sup.3+, β-SiAlON:Eu.sup.2+, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+, (Li,Na,K).sub.2(Ti,Zr,Si,Ge)F.sub.6:Mn.sup.4+ and (Ca,Sr,Ba)MgAl.sub.10O.sub.17:Eu.sup.2+. The sign “,” in between the various elements indicates that the element or elements within the parenthesis may be a single component or a solid solution comprising two or more elements for instance, (Ca,Sr)AlSiN.sub.3:Eu.sup.2+ stands for one or more solid solutions in CaAlSiN.sub.3:Eu.sup.2+, SrAlSiN.sub.3:Eu.sup.2+ and Ca.sub.1-xSr.sub.xAlSiN.sub.3:Eu.sup.2+ (0<x<1). Use of the phosphor according to the present application in cooperation with the aforementioned phosphors enables light emitting devices to emit white light with high emission efficiency, high color rendering index and low chromatic temperature, these white-light light emitting devices being applicable to the field of illumination or display.

(21) Advantageous effects of the present application are explained in further detail below in conjunction with Examples and Comparative Examples.

Example 1

(22) Basing on the stoichiometric proportion of Lu.sub.2.9Si.sub.6N.sub.11:0.1Ce.sup.3+, source materials of LuN (99.9%), Si.sub.3N.sub.4 (99.9%) and CeO.sub.2 (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.9Si.sub.6N.sub.11:0.1Ce.sup.3+ phosphor of Example 1. The phosphor is subjected to X-ray scanning to arrive at FIG. 1, in which the Bragg angles scanned are 10 to 68°, and the scanning rate is 6°/min; the phosphor is subjected to fluorescence spectrum test, with excitation monitor wavelength as 490 nm, and emission monitor wavelength as 440 nm see FIG. 2 for the monitor result.

(23) As can be seen from the result of FIG. 1, Lu.sub.2.9Si.sub.6N.sub.11:0.1Ce.sup.3+ of the present application as the same crystal structure as Y.sub.3Si.sub.6N.sub.11.

Example 2

(24) The Lu.sub.2.9Si.sub.6N.sub.11:0.1Ce.sup.3+ obtained in Example 1, a white LED yellow fluorescent material Y.sub.3Al.sub.5O.sub.12:Ce+.sup.3, and a red fluorescent material CaAlSiN.sub.3:Eu.sup.2+ are mixed at a mass ratio of 15:70:15 and put in silica gel to form a sticky substance; the sticky substance is coated on a 430 nm blue LED chip to obtain a white-light LED device; the white-light LED device is tested, by a remote SIS-3_1.0m steel photometric integrating sphere R98, with drive current of 60 mA, to show the test results of a color rendering index as 86, a color coordinate as (0.32,0.36), and an emission efficiency as 140 1 m/W.

Comparative Example 1

(25) Basing on the stoichiometric proportion La.sub.2.86Si.sub.6N.sub.11:0.14Ce.sup.3+, source materials of 43.76 g LaN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 2.156 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain La.sub.2.86Si.sub.6N.sub.11:0.14Ce.sup.3+ phosphor of Comparative Example 1.

Comparative Example 2

(26) Basing on the stoichiometric proportion Y.sub.2.9Si.sub.6N.sub.11:0.1Ce.sup.3+, source materials of 29.87 g LaN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 1.54 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product.

(27) The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Y.sub.2.9Si.sub.6N.sub.11:0.1Ce.sup.3+ phosphor of Comparative Example 2.

Example 3

(28) Basing on the stoichiometric proportion of Lu.sub.2.1Si.sub.6N.sub.11:0.9Ce.sup.3+, source materials of 39.69 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 13.86 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.1Si.sub.6N.sub.11:0.9Ce.sup.3+ phosphor of Example 3.

Example 4

(29) Basing on the stoichiometric proportion of Lu.sub.2.2Si.sub.6N.sub.11:0.8Ce.sup.3+, source materials of 41.58 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 12.32 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.2Si.sub.6N.sub.11:0.8Ce.sup.3+ phosphor of Example 4.

Example 5

(30) Basing on the stoichiometric proportion of Lu.sub.2.2Si.sub.6N.sub.11:0.7Ce.sup.3+, 0.1Dy.sup.3+, source materials of 39.69 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%), 10.78 g CeN (99.99%) and 2.19 g DyF.sub.3 (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.2Si.sub.6N.sub.11:0.7Ce.sup.3+, 0.1Dy.sup.3+ phosphor of Example 5.

Example 6

(31) Basing on the stoichiometric proportion of La.sub.1.16Lu.sub.1.74Si.sub.6N.sub.11:0.1Ce.sup.3+, source materials of 17.88 g LaN (99.9%), 32.89 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 1.54 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain La.sub.1.16Lu.sub.1.74Si.sub.6N.sub.11:0.1 Ce.sup.3+ phosphor of Example 6.

Example 7

(32) Basing on the stoichiometric proportion of La.sub.0.7375Lu.sub.2.2125Si.sub.6N.sub.11:0.05Ce.sup.3+, source materials of 11.28 g LaN (99.9%), 41.82 g LuN (99.9%), 28.56 g Si.sub.3Na (99.9%) and 0.77 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain La.sub.0.7375Lu.sub.2.2125Si.sub.6N.sub.11:0.05Ce.sup.3+ phosphor of Example 7.

Example 8

(33) Basing on the stoichiometric proportion of La.sub.0.575Lu.sub.2.325Si.sub.6N.sub.11:0.1Ce.sup.3+, source materials of 8.8 g LaN (99.9%), 43.85 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 1.54 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain La.sub.0.575Lu.sub.2.325Si.sub.6N.sub.11:0.1Ce.sup.3+ phosphor of Example 8.

Example 9

(34) Basing on the stoichiometric proportion of Lu.sub.3Si.sub.5N.sub.10:0.3Ce.sup.3+, source materials of 56.7 g LuN (99.9%), 23.38 g Si.sub.3N.sub.4 (99.9%) and 4.63 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.3Si.sub.5N.sub.10:0.3Ce.sup.3+ phosphor of Example 9.

Example 10

(35) Basing on the stoichiometric proportion of Lu.sub.2.57Si.sub.7N.sub.12:0.1Ce.sup.3+, source materials of 48.57 g LuN (99.9%), 32.7 g Si.sub.3N.sub.4 (99.9%) and 1.54 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.57Si.sub.7N.sub.12:0.1Ce.sup.3+ phosphor of Example 10.

Example 11

(36) Basing on the stoichiometric proportion of Lu.sub.3.07Si.sub.5.5N.sub.10.5:0.1Ce.sup.3+, source materials of 58.023 g LuN (99.9%), 23.67 g Si.sub.3N.sub.4 (99.9%) and 1.54 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.3.07Si.sub.5.5N.sub.10.5:0.1Ce.sup.3+ phosphor of Example 11.

Example 12

(37) Basing on the stoichiometric proportion of Lu.sub.2.73Si.sub.6.5N.sub.11.5:0.1Ce.sup.3+, source materials of 51.6 g LuN (99.9%), 30.33 g Si.sub.3N.sub.4 (99.9%) and 1.54 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.73Si.sub.6.5N.sub.11.5:0.1Ce.sup.3+ phosphor of Example 12.

Example 13

(38) Basing on the stoichiometric proportion of Lu.sub.25Si.sub.6N.sub.11:0.5Ce.sup.3+, source materials of 47.25 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 7.7 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.25Si.sub.6N.sub.11:0.5Ce.sup.3+ phosphor of Example 13.

Example 14

(39) Basing on the stoichiometric proportion of Lu.sub.2.86Si.sub.6N.sub.11:0.14Ce.sup.3+, source materials of 54.05 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 2.156 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.286Si.sub.6N.sub.11:0.14Ce.sup.3+ phosphor of Example 14.

Example 15

(40) Basing on the stoichiometric proportion of Lu.sub.2.8Si.sub.6N.sub.11:0.2Ce.sup.3+, source materials of 52.92 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 3.08 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.8Si.sub.6N.sub.11:0.2Ce.sup.3+ phosphor of Example 15.

Example 16

(41) Basing on the stoichiometric proportion of Lu.sub.27Si.sub.6N.sub.11:0.3Ce.sup.3+, source materials of 51.03 g LuN (99.9%), 28.56 g Si.sub.3N.sub.4 (99.9%) and 4.62 g CeN (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.27Si.sub.6N.sub.11:0.3Ce.sup.3+ phosphor of Example 16.

Example 17

(42) Basing on the stoichiometric proportion of Lu.sub.2.86Si.sub.5.9N.sub.10.5O.sub.0.5:0.14Ce.sup.3+, source materials of 54.05 g LuN (99.9%), 26.4 g Si.sub.3N.sub.4 (99.9%), 2.156 g CeN (99.99%) and 1.5SiO.sub.2 (99.99%) are precisely weighted, and mixed to form a mixed source material. The mixed source material is fully mixed and ground in a glove compartment for 30 minutes to obtain a mixture. The mixture is heated at a heating rate of 10° C./min to 1850° C. under pure nitrogen environment, then held at 1850° C. for 10 hours, and subsequently naturally cooled to obtain a calcinated product. The calcinated product is taken out to be crushed, washed, sieved and baked to obtain Lu.sub.2.86Si.sub.5.9N.sub.10.5O.sub.0.5:0.14Ce.sup.3+ phosphor of Example 17.

(43) Test results of emission peak wavelengths, external quantum efficiencies and packaging color rendering indices of the phosphors in the above Examples are shown in the following Table 1, in which quantum efficiencies are tested by a QE-2100 quantum efficiency meter, with BaSO.sub.4 being selected as guide sample for comparison, and coloring indices are tested by HAAS2000.

(44) TABLE-US-00001 TABLE 1 Proportional Compositions of Various Elements in Comparative Examples and Examples EPW EQE M R D a x y nm % C. Ex- La Ce N 0.14 6 11 535 98.7 ample 1 C. Ex- Y Ce N 0.1 6 11 550 58.2 ample 2 Exam- Lu Ce N 0.9 6 11 540 65.1 ple 3 Exam- Lu Ce N 0.8 6 11 536 68.5 ple 4 Exam- Lu Ce + Dy N 0.8 6 11 535 67.3 ple 5 Exam- La + Lu Ce N 0.1 6 11 530 78.1 ple 6 Exam- La + Lu Ce N 0.05 6 11 524 77.6 ple 7 Exam- La + Lu Ce N 0.1 6 11 518 83.8 ple 8 Exam- Lu Ce N 0.3 5 10 488 77.2 ple 9 Exam- Lu Ce N 0.1 7 12 479 76.8 ple 10 Exam- Lu Ce N 0.1 5.5 10.5 480 73.8 ple 11 Exam- Lu Ce N 0.1 6.5 11.5 482 74.3 ple 12 Exam- Lu Ce N 0.5 6 11 510 78.5 ple 13 Exam- Lu Ce N 0.14 6 11 485 80.3 ple 14 Exam- Lu Ce N 0.2 6 11 490 78.2 ple 15 Exam- Lu Ce N 0.3 6 11 496 78.6 ple 16 Exam- Lu Ce N + O 0.14 5.9 11 483 76.2 ple 17 (EPW stands for Emission Peak Wavelength; EQE stands for External Quantum Efficiency)

(45) As should be pointed out here, a, x, y respectively stand for stoichiometric ratios corresponding to different elements in the specific molecular formulae of the samples in the various Examples.

(46) As can be seen from the data in the above Table 1, the emission peak wavelengths of the phosphors having the composition according to the present application in Examples 3 to 17 all lie within the wavelength range of 460 to 540 nm; moreover, as can be seen from the comparison between Examples 3 and 4, with the increase in the content of the Lu element, blue shift occurs in the emission wavelength; as can be seen from the comparison between Examples 4 and 5, when Ce and Dy are simultaneously used, emission peak wavelengths and external quantum efficiencies are not apparently changed, but Dy.sup.3+ has stronger emission at the yellow region the addition of suitable amount of Dy.sup.3+ helps improve the photochromic property of phosphors; as can be seen from the comparison between Examples 6 and 8, when Lu and La are simultaneously used, the change in the content of Lu obviously affects the emission wavelength with the increase in its content, blue shift occurs in the emission wavelength.

(47) Moreover, the X-ray scanning results of the phosphors specified in the above Examples 3 through 17 all show the same diffraction peak peaking positions and similar strengths as those in FIG. 1, that is to say, it can be judged that they have the same crystal structure as Y.sub.3Si.sub.6N.sub.11.

(48) Referring to FIG. 3, a light emitting device 301 includes a fluorescent substance 303 and an excitation light source 306, and that the fluorescent substance 303 have the lutetium nitride-based phosphor 309.

(49) As can be seen from the above description, the aforementioned Examples of the present invention achieve the following technical effects: since the ion radius of Lu.sup.3+ is smaller than that of La.sup.3+, when the inorganic compound forming the phosphor comprises element Lu, the original ligand site would be contracted; in order to reduce lattice distortion due to the ligand site contraction, the adjacent ligand site expands, and this weakens the existing crystal field environment, so that the emission spectrum of the lutetium nitride-based phosphor having the inorganic compound can be easily adjusted—even adjusted to the green light region, and therefore its photochromic property can be flexibly adjusted according to needs; at the same time, since the content of the Lu element is greater than 50%, the main component of the inorganic compound is changed, that is to say, the originally substituted element is changed to the Lu element, and such change ameliorates lattice distortion and forms single crystal grains of relatively uniform formations the single crystal grains have long-range order, i.e., the inorganic compound achieves better crystallization properties; furthermore, its thermal stability is relatively good to the extent that the need for high-density energy excitation can be satisfied.

(50) Since the difference between ion radii Lu.sup.3+ (0.848 Å) and Ce.sup.3+ (1.03 Å) is greater than the difference between ion radii La.sup.3+ (1.06 Å) and Ce.sup.3+ (1.03 Å), after the aforementioned inorganic compound has been doped with small amount of Ce.sup.3+, lattice distortion is partially strengthened due to the relatively great difference between Ce and Lu ion radii, thereby leading to increase in the crystal field strength, and, at the same time, there are two types of Lu lattice sites with relatively great difference in partial ligand site environments in the inorganic compound. On the basis of the above two points, 5d energy level splitting of Ce.sup.3+ is enhanced, whereby the adjustability flexibility of the emission spectrum of the inorganic compound is further enhanced.

(51) What the above recited are merely preferred examples of the present invention, and they are not meant to restrict the present invention, as persons skilled in the art may make various modifications and variations to the present invention. Any amendment, equivalent substitution or improvement made within the spirit and principle of the present invention shall all be covered within the protection scope of the present invention.