examples of the present inventive concept will be described below in more detail with reference to the accompanying drawings . the examples of the present inventive concept may , however , be embodied in different forms and should not be construed as limited to the examples set forth herein . like reference numerals may refer to like elements throughout the specification . fig1 illustrates a flowchart conceptually showing a method for manufacturing a nitride - based phosphor according to example embodiments of the present inventive concept . referring to fig1 , first , a plurality of precursors may be prepared to manufacture the nitride - based phosphor . the plurality of precursors may be divided into two groups , that is , a first group and a second group . the first group may include an m precursor containing at least one of ca , sr , and ba , and a first si precursor . the second group may include an eu precursor and a second si precursor . alternatively , the plurality of precursors may be divided into three or more groups . the m precursor may include metal carbonate ( mco 3 ). the first si precursor may include sio 2 . the eu precursor may be eu 2 o 3 . the second si precursor may include sio 2 and si 3 n 4 . thus , the first si precursor and the second si precursor may both include the same precursor , that is , sio 2 . the precursors of each group undergo a mixing process . any of a dry mixing method or a wet mixing method may be used to mix the precursors . for example , according to the wet mixing method , the precursors may be mixed along with a solvent and a ball that assists grinding . the ball may be made of si 3 n 4 , al 2 o 3 , zro 2 , or the like . the solvent may be a deionized ( di ) water , an alcohol such as ethanol , or an organic solvent such as n - hexane . the precursors may be sealed along with the solvent and the ball , and uniformly mixed by a miller or the like . a mixture generated by the mixing process may be separated from the ball . the solvent may be mostly vaporized by a drying process using an oven . powder remaining after the drying process may be uniformly ground into micrometer particles using a sieve made of metal or polymer . according to the dry mixing method , the precursors may be put in a container without a solvent and uniformly mixed by a milling machine . here , a ball may also be used to promote the mixing . the dry mixing method may reduce the processing time compared to the wet mixing time because a solvent drying process is omitted . as in the wet mixing method , powder remaining after the mixing of the precursors may be uniformly ground into a desired size using a sieve made of metal or polymer . the mixed precursors of each group respectively may undergo a first sintering operation . after the first sintering operation , a first sintered product and a second sintered product may be produced as intermediate products . the first sintered product and the second sintered product are mixed by the above - described mixing methods and go through a second sintering operation , thereby obtaining a final phosphor . in the second sintering operation , an additional si precursor or a flux may be added before the mixing . the flux may facilitate movement among the first sintered product , the second sintered product , and the additional si precursor added in the second sintering operation , thereby improving crystallinity and grain growth of the nitride - based phosphor , that is , a final product . a sintering temperature of the second sintering operation may be higher than a sintering temperature of the first sintering operation . the second sintering operation may be performed under a nitrogen and oxygen gas atmosphere . hereinafter , a description will be made about a method for manufacturing a nitride - based yellow phosphor having a composition formula m 1 - z eu z si a o b n c ( m = sr 1 - x - y ba x ca y , 0 ≦ x ≦ 0 . 5 , 0 ≦ y ≦ 0 . 2 , 0 & lt ; z ≦ 0 . 3 , 2 ≦ a ≦ 2 . 5 , 1 . 5 ≦ b ≦ 2 , and 2 ≦ c ≦ 2 . 5 ). as described above , the first group may include the m precursor containing at least one of ca , sr , and ba , and the first si precursor . the second group may include the eu precursor and the second si precursor . the m precursor may include metal carbonate ( mco 3 ). the first si precursor may include sio 2 . the eu precursor may be eu 2 o 3 . the second si precursor may include sio 2 or si 3 n 4 . after the mixing is completed , the precursors of the first group are sintered at temperature of about 900 ° c . to about 1300 ° c . the sintering of the precursors of the first group may be performed under air atmosphere for about 3 hours . the precursors of the second group may be sintered at temperature of about 1200 ° c . to about 1400 ° c ., and under a nitrogen and hydrogen gas atmosphere . the precursors of the second group may be sintered also for about 3 hours . when the precursors are used , a sintered product of the first group may contain m 2 sio 4 while a sintered product of the second group may contain eusi 2 o 2 n 2 . as described above , when the intermediate products of m 2 sio 4 and eusi 2 o 2 n 2 are formed in advance and used as raw materials of si and eu , respectively , production of impurities may be restrained . accordingly , even though concentration of eu increases , the nitride - phosphor may be synthesized in a single phase . the intermediate product m 2 sio 4 is easy to synthesize in a single phase in the atmosphere . since intermediate product m 2 sio 4 enables synthesis of a solid solution containing at least two kinds of m ions , a nitride - based phosphor containing at least two kinds of m ions may also be synthesized . another intermediate product eusi 2 o 2 n 2 may restrain increase of oxygen in a starting composition by fixing a composition ratio among eu 2 o 3 , sio 2 and si 3 n 4 which are starting materials . therefore , the phosphor may be synthesized in a single phase without producing impurities . also , since eusi 2 o 2 n 2 is used as a raw material of eu , oxygen in a feed composition does not increase even though concentration of eu increases . therefore , production of impurities may be restrained , and a phosphor having a composition formula m 1 - z eu z si a o b n c ( m = sr 1 - x - y ba x ca y , 0 ≦ x ≦ 0 . 5 , 0 ≦ y ≦ 0 . 3 , 2 & lt ; z ≦ 0 . 3 , 2 ≦ a ≦ 2 . 5 , 1 . 5 ≦ b ≦ 2 , and 2 ≦ c ≦ 2 . 5 ) may be generated in a single phase . before the second sintering operation , the intermediate products m 2 sio 4 and eusi 2 o 2 n 2 may be mixed along with the additional si precursor and the flux according to the above - described mixing method . the additional si precursor may be si 3 n 4 . the flux may be nh 4 a ( a denotes at least one of f and cl ), de 2 d denotes at least one of cu , sr , and ba , and e denotes at least one of f and cl ), le ( l denotes at least one of na and k and e denotes at least one of f and cl ), or the like . the flux may promote movement of m 2 sio 4 , eusi 2 o 2 n 2 , and si 3 n 4 , thereby improving crystallinity and grain growth of msi 2 o 2 n 2 : eu 2 + . accordingly , the emission intensity of the phosphor may be increased . the second sintering operation may be performed under a nitrogen and hydrogen gas atmosphere , at a sintering temperature of about 1300 ° c . to about 1600 ° c . hereinafter , a nitride - base phosphor manufactured by the above method will be described . the nitride - base phosphor according to the example embodiments of the present inventive concept may be expressed by a composition formula m 1 - z eu z si a o b n c ( m = sr 1 - x - y ba x ca y , 0 ≦ x ≦ 0 . 5 , 0 ≦ y ≦ 0 . 2 , 0 & lt ; z ≦ 0 . 3 , 2 ≦ a ≦ 2 . 5 , 1 . 5 ≦ b ≦ 2 , and 2 ≦ c ≦ 2 . 5 ). the nitride - based phosphor may be a single - phase yellow phosphor . with respect to the whole phosphor , concentration of an oxynitride having an atomic ratio of o / n & gt ; 1 may be 1 mol % or less . depending on embodiments of the present inventive concept , the nitride - base phosphor may substantially include only a single phase . during manufacturing of the nitride - base phosphor according to example embodiments of the present inventive concept , an oxynitride of an impurity , such as m 3 si 6 o 9 n 4 , may not be produced . in addition , eusi 2 o 2 n 2 , which is an intermediate sintered product generated during the manufacturing , may restrain increase of oxygen in the starting composition by fixing the composition ratio among eu 2 o 3 , sio 2 and si 3 n 4 which are starting materials . accordingly , the phosphor may be synthesized in a single phase without production of impurities . when a light emitting diode ( led ) is driven , the nitride - based phosphor under a temperature condition of about 150 ° c . to about 200 ° c . may have at least 80 % emission intensity of an emission intensity under normal temperature , which corresponds to almost 90 % of an emission intensity of a conventional yttrium aluminum garnet ( yag ) phosphor . therefore , the nitride - based phosphor has excellent high - temperature stability and high emission characteristics . that is , application characteristic of the nitride - based phosphor with respect to the led is more excellent compared to the conventional yag phosphor . hereinafter , a nitride - based phosphor manufacturing method according to example embodiments of the present inventive concept will be described in detail . a first embodiment of the present inventive concept suggests a method for manufacturing a phosphor ( sr 0 . 75 ba 0 . 25 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 . fig2 is a flowchart illustrating the phosphor manufacturing method according to the first embodiment of the present inventive concept . the phosphor of the first embodiment of the present inventive concept is manufactured according to an order shown in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . likewise , precursors eu 2 o 3 , sio 2 and si 3 n 4 belonging to a second group are mixed , and sintered for about 3 hours at temperature of about 1300 ° c . under a nitrogen and hydrogen gas atmosphere , thereby obtaining an intermediate sintered product eusi 2 o 2 n 2 . next , the intermediate sintered products m 2 sio 4 and eusi 2 o 2 n 2 are mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . thus - generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a phosphor having a composition formula ( sr 0 . 75 ba 0 . 25 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 as a final product . the present comparison example also suggests a method for manufacturing a phosphor ( sr 0 . 75 ba 0 . 25 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 , that is , a nitride - based phosphor . however , the phosphor of the present comparison example is manufactured according to a method shown in fig3 , which is different from the method of fig2 . referring to fig3 , all precursors including mco 3 ( srco 3 , baco 3 ), sio 2 , eu 2 o 3 , and si 3 n 4 are simultaneously mixed , and sintered at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , in the same manner as in the second sintering operation of the first embodiment of the present inventive concept , and for about 6 hours , thereby obtaining a phosphor having a composition formula ( sr 0 . 75 ba 0 . 25 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 as a final product . a yag : ce 3 + phosphor of merck , which is commercially available , is used as a phosphor of the second comparison example . in table 1 below , the phosphors of the first embodiment of the present inventive concept , the first comparison example , and the second comparison example are listed . fig4 illustrates a graph showing an emission intensity according to temperature , regarding the phosphor manufactured in the first embodiment of the present inventive concept and the phosphor manufactured in the second comparison example . referring to fig4 , at about 150 ° c . to about 200 ° c . which is a general led driving temperature , the emission intensity of the phosphor of the first embodiment of the present inventive concept is at least 80 % of an emission intensity under normal temperature , compared to a yag phosphor of the second comparison example . considering that the yag phosphor of the second comparison example has about 60 % emission intensity of the normal temperature emission intensity , the phosphor of the first embodiment of the present inventive concept is proved to have about 20 % superior characteristic to the yag phosphor of the second comparison example . fig5 illustrates emission spectrums of the phosphor of the first embodiment of the present inventive concept , the phosphor of the first comparison example , and the phosphor of the second comparison example . referring to fig5 , the phosphor of the first embodiment of the present inventive concept shows at least twice as high emission intensity ( integral intensity ) as the phosphor of the first comparison example synthesized by the conventional solid phase method . in addition , the phosphor of the first embodiment of the present inventive concept shows about 90 % emission intensity of the emission intensity of the yag phosphor of the second comparison example . that is , the phosphor of the first embodiment of the present inventive concept has the sufficient emission intensity to replace the yag phosphor . the phosphor of the first embodiment of the present inventive concept has an excellent emission intensity compared to the phosphor synthesized by the conventional solid phase method in the second comparison example , and also has an excellent high - temperature stability compared to the phosphor of the second comparison example . especially , the phosphor of the first embodiment of the present inventive concept has similar emission characteristic to the yag phosphor , while having the excellent high - temperature stability . that is , the phosphor of the first embodiment of the present inventive concept has high applicability to the led . thus , the phosphor of the first embodiment of the present inventive concept is expected to stably replace the conventional yag phosphor . hereinafter , the led to which is applied the nitride - based phosphor according to example embodiments of the present inventive concept will be described with reference to the accompanying drawings . fig6 illustrates a sectional view showing a structure of a white led according to example embodiments of the present inventive concept . referring to fig6 , the white led using a blue led or a long - wavelength ultraviolet ( uv ) led may include a reflection cup 611 , an ingan - based led chip 613 ( gan - based led in case of the long - wavelength uv led ) installed on the reflection cup 611 , a yellow phosphor 617 excited by light emitted from the led chip 613 , electrode line 615 connected to the led chip 613 , and a light - transmitting epoxy 619 sealing the led chip 613 . the yellow phosphor 617 may function as a wavelength converting material . the above - described nitride - based phosphor according to embodiments of the present inventive concept may be used as the yellow phosphor 617 . the ingan - based led chip 613 may be connected with an external power supply by the electrode line 615 . the yellow phosphor 617 excited by the light emitted from the ingan - based led chip 613 may be mixed with the light - transmitting epoxy 619 and disposed at the outside of the led chip 613 . however , the present inventive concept is not limited to the structure shown in fig1 , the led may have various structures where components are properly added , altered , and omitted . also , the yellow phosphor 617 may be mixed with silicone , besides the epoxy , and molded around the led chip 613 , thereby forming the white led . that is , the yellow phosphor 617 may be disposed at the outside of the led chip 613 such that the light emitted from the led chip 613 functions to excite the yellow phosphor 617 . procedures for forming a white light will be described in detail . a blue light emitted from the led chip 613 may be passed through the yellow phosphor 617 according to the above - described example embodiments of the present inventive concept . part of the blue light may excite the yellow phosphor 617 , thereby forming a yellow light , while the rest part of the blue light may be passed as it is . thus , the white light may be formed as the excited yellow light and the blue light overlap each other . hereinafter , a nitride - based phosphor manufactured in the foregoing manner will be described in detail . a nitride - based phosphor manufactured in embodiment 2 of the present inventive concept is a mixed - phase phosphor generated from an initial composition ( sr 0 . 71 ba 0 . 29 ) 0 . 92 eu 0 . 08 si 2 o 2 n 2 . in the same manner as in embodiment 1 of the present inventive concept , the phosphor of embodiment 2 of the present inventive concept is manufactured in the order illustrated in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . likewise , precursors eu 2 o 3 , sio 2 and si 3 n 4 belonging to a second group are mixed , and sintered for about 3 hours at temperature of about 1300 ° c . under a nitrogen and hydrogen gas atmosphere , thereby obtaining an intermediate sintered product eusi 2 o 2 n 2 . next , the intermediate sintered products m 2 sio 4 and eusi 2 o 2 n 2 are mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . the generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a mixed - phase phosphor as a final product . the manufactured phosphor is washed using 5 % ( v / v ) hno 3 solution and deionized ( di ) water , thereby removing impurities and an intermediate phase . an x - ray diffraction ( xrd ) pattern and an emission wavelength of the above - manufactured phosphor are shown in fig7 a and 7b . referring to fig7 a , since two types of main diffraction peaks are observed , it is determined that two types of xrd patterns are simultaneously shown . accordingly , it may be understood that the phosphor of embodiment 2 of the present inventive concept is a mixed - phase phosphor including two different phosphors . as shown in fig7 b , by excitation of light of about 450 nm which is a typical wavelength of a blue led , the phosphor of embodiment 2 of the present inventive concept shows an emission spectrum in a range of about 460 nm to 760 nm and an emission peak of about 554 nm . according to such optical properties , the phosphor of embodiment 2 of the present inventive concept shows yellow emission , which means that the phosphor of embodiment 2 of the present inventive concept has emission characteristics enough to replace the yag phosphor . a nitride - based phosphor manufactured in embodiment 3 of the present inventive concept is a mixed - phase phosphor generated from an initial composition ( sr 0 . 65 ba 0 . 35 ) 0 . 88 eu 0 . 12 si 2 o 2 n 2 . in the same manner as in embodiment 1 of the present inventive concept , the phosphor of embodiment 3 of the present inventive concept is manufactured in the order illustrated in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . likewise , precursors eu 2 o 3 , sio 2 and si 3 n 4 belonging to a second group are mixed , and sintered for about 3 hours at temperature of about 1300 ° c . under a nitrogen and hydrogen gas atmosphere , thereby obtaining an intermediate sintered product eusi 2 o 2 n 2 . next , the intermediate sintered products m 2 sio 4 and eusi 2 o 2 n 2 are mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . the generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a mixed - phase phosphor as a final product . the manufactured phosphor is washed using 5 % ( v / v ) fino 3 solution and di water , thereby removing impurities and an intermediate phase . an xrd pattern and an emission wavelength of the above - manufactured phosphor are shown in fig8 a and 8b . referring to fig8 a , since two types of main diffraction peaks are observed , it is determined that two types of xrd patterns are simultaneously shown . accordingly , it may be understood that the phosphor of embodiment 3 of the present inventive concept is a mixed - phase phosphor including two different phosphors . as shown in fig8 b , by excitation of light of about 450 nm which is a typical wavelength of a blue led , the phosphor of embodiment 3 of the present inventive concept shows an emission spectrum in a range of about 460 nm to 760 nm and an emission peak of about 560 nm . according to such optical properties , the phosphor of embodiment 3 of the present inventive concept shows yellow emission , which means that the phosphor of embodiment 3 of the present inventive concept has enough emission characteristics to replace the yag phosphor . a nitride - based phosphor manufactured in embodiment 4 of the present inventive concept has a composition formula ( sr 0 . 31 ba 0 . 69 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 . in the same manner as in embodiment 1 of the present inventive concept , the phosphor of embodiment 4 of the present inventive concept is manufactured in the order illustrated in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . likewise , precursors eu 2 o 3 , sio 2 and si 3 n 4 belonging to a second group are mixed , and sintered for about 3 hours at temperature of about 1300 ° c . under a nitrogen and hydrogen gas atmosphere , thereby obtaining an intermediate sintered product eusi 2 o 2 n 2 . next , the intermediate sintered products m 2 sio 4 and eusi 2 o 2 n 2 are mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . the generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a single - phase phosphor having a composition formula ( sr 0 . 31 ba 0 . 69 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 as a final product . next , the manufactured phosphor is washed using 5 % ( v / v ) hno 3 solution and di water , thereby removing impurities and an intermediate phase . an xrd pattern and an emission wavelength of the above - manufactured phosphor are shown in fig9 a and 9b . referring to fig9 a , since a single type of main diffraction peak is observed , it is determined that the xrd pattern is shown according to the single phase . accordingly , it may be understood that the phosphor of embodiment 4 of the present inventive concept is a single - phase phosphor . as shown in fig9 b , by excitation of light of about 450 nm which is a typical wavelength of a blue led , the phosphor of embodiment 4 of the present inventive concept shows an emission spectrum in a range of about 465 nm to 765 nm and an emission peak of about 577 nm . according to such optical properties , the phosphor of embodiment 4 of the present inventive concept shows yellow emission , which means that the phosphor of embodiment 4 of the present inventive concept has sufficient emission characteristics to replace the yag phosphor . a nitride - based phosphor manufactured in embodiment 5 of the present inventive concept is a single - phase phosphor having a composition formula ( sr 0 . 35 ba 0 . 65 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 . in the same manner as in embodiment 1 of the present inventive concept , the phosphor of embodiment 5 of the present inventive concept is manufactured in the order illustrated in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . likewise , precursors eu 2 o 3 , sio 2 and si 3 n 4 belonging to a second group are mixed , and sintered for about 3 hours at temperature of about 1300 ° c . under a nitrogen and hydrogen gas atmosphere , thereby obtaining an intermediate sintered product eusi 2 o 2 n 2 . next , the intermediate sintered products m 2 sio 4 and eusi 2 o 2 n 2 are mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . the generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a single - phase phosphor having a composition formula ( sr 0 . 35 ba 0 . 65 ) 0 . 85 eu 0 . 15 si 2 o 2 n 2 as a final product . next , the manufactured phosphor is washed using 5 % ( v / v ) hno 3 solution and di water , thereby removing impurities and an intermediate phase . crystal - structure analysis data of the above - manufactured phosphor is shown in table 2 . a rietveld fitting result of the phosphor is shown in fig1 . referring to table 2 , it may be understood that the nitride - based phosphor manufactured in embodiment 5 of the present inventive concept has a triclinic crystal system and a space group of p1 . referring to fig1 , an xrd pattern of the nitride - based phosphor of embodiment 5 of the present inventive concept nearly corresponds to a calculated value . accordingly , it may be determined that the phosphor of embodiment 5 of the present inventive concept is a single - phase phosphor . in fig1 , ‘ obs ’ refers to a measured value of the manufactured phosphor , ‘ cal ’ refers to a calculated value obtained through calculation , and ‘ diff ( obs - cal )’ refers to a value obtained by subtracting the calculated value from the measured value , from which a degree of purity of the manufactured phosphor may be determined . embodiments 6 to 26 of the present inventive concept are related to phosphors having a composition formula ( sr 1 - m ba m ) si 2 o 2 n 2 where values of ‘ m ’ are 0 , 0 . 05 , 0 . 1 , 0 . 15 , 0 . 2 , 0 . 25 , 0 . 3 , 0 . 35 , 0 . 4 , 0 . 45 , 0 . 5 , 0 . 55 , 0 . 6 , 0 . 65 , 0 . 7 , 0 . 75 , 0 . 8 , 0 . 85 , 0 . 9 , 0 . 95 , and 1 , respectively . in the same manner as in embodiment 1 of the present inventive concept , the phosphors of embodiments 6 to 26 of the present inventive concept are manufactured in the order illustrated in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . here , since eu is not included , a process of synthesizing another intermediate sintered product eusi 2 o 2 n 2 is omitted . next , the intermediate sintered products m 2 sio 4 is mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . the generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a phosphor having a composition formula ( sr 1 - m ba m ) si 2 o 2 n 2 ( where ‘ m ’ has values between 0 and 1 as aforementioned ) as a final product . next , the manufactured phosphor is washed using 5 % ( v / v ) hno 3 solution and di water , thereby removing impurities and an intermediate phase . xrd patterns of the above - manufactured phosphors are shown in fig1 . referring to fig1 , the xrd patterns are regularly changed according to an increase in ba content . therefore , differences in a crystal phase according to the increase in ba content may be distinguished . changes in the crystal phase according to a range of ba content are shown in table 3 . embodiments 27 to 41 of the present inventive concept are related to phosphors having a composition formula ( sr 1 - m ba m ) 1 - n eu n si 2 o 2 n 2 in which values of ( m , n ) are ( 0 , 0 . 02 ), ( 0 . 3 , 0 . 2 ), ( 0 . 4 , 0 . 15 ), ( 0 . 6 , 0 . 1 ), ( 0 . 6 , 0 . 2 ), ( 0 . 7 , 0 . 05 ), ( 0 . 8 , 0 . 02 ), ( 0 . 8 , 0 . 05 ), ( 0 . 8 , 0 . 1 ), ( 0 . 8 , 0 . 15 ), ( 0 . 8 , 0 . 2 ), ( 0 . 9 , 0 . 1 ), ( 1 , 0 . 02 ), ( 1 , 0 . 1 ), and ( 1 , 0 . 15 ), respectively . in the same manner as in embodiment 1 of the present inventive concept , the phosphors of embodiments 27 to 41 of the present inventive concept are manufactured in the order illustrated in fig2 . referring to fig2 , precursors mco 3 ( srco 3 , baco 3 ) and sio 2 belonging to a first group are mixed , and sintered for about 3 hours at temperature of about 1100 ° c . under air atmosphere , thereby obtaining an intermediate sintered product m 2 sio 4 . likewise , precursors eu 2 o 3 , sio 2 and si 3 n 4 belonging to a second group are mixed , and sintered for about 3 hours at temperature of about 1300 ° c . under a nitrogen and hydrogen gas atmosphere , thereby obtaining an intermediate sintered product eusi 2 o 2 n 2 . next , the intermediate sintered products m 2 sio 4 and eusi 2 o 2 n 2 are mixed with si 3 n 4 that is an additional si precursor and nh 4 cl that is a flux . the generated mixture is sintered again at temperature of about 1400 ° c . under a nitrogen and hydrogen gas atmosphere , thereby manufacturing a single - phase phosphor having a composition formula ( sr 1 - m ba m ) 1 - n eu n si 2 o 2 n 2 ( where m and n have the aforementioned values ), as a final product . next , the manufactured phosphor is washed using 5 % ( v / v ) hno 3 solution and di water , thereby removing impurities and an intermediate phase . xrd patterns and emission spectrums of the phosphors are shown in fig1 a and 12b . referring to fig1 a , the xrd patterns are regularly changed according to contents of ba and eu . therefore , differences in a crystal phase according to the contents of ba and eu may be distinguished . changes in the crystal phase according to a range of contents of ba and eu are shown in table 4 . in addition , referring to fig1 b , the emission wavelength is changed according to the contents of ba and eu , corresponding to the changes in the xrd pattern . furthermore , as a result of analysis of phases and emission peak wavelengths wp of the phosphors manufactured in embodiments 27 to 41 of the present inventive concept are shown in table 4 . also , changes in the phase according to the range of m and n values from the xrd patterns of the phosphors manufactured in embodiments 6 to 26 of the present inventive concept and embodiments 27 to 41 of the present inventive concept are shown in table 3 . referring to tables 3 and 4 , a plurality of phases mixedly exist . in general phosphors , changes of a plurality of phases rarely occur according to the changes in a ratio of sr and ba between sr and ba . however , embodiments of the present inventive concept show that changes of the plurality of phases occur . furthermore , the overall xrd pattern is constant even with changes in the m and n values . also , it may be understood that the phase is a solid solution when the structures are similar although a diffraction angle ( 2θ ) slightly changes . although a few example embodiments of the present inventive concept have been shown and described , the present inventive concept is not limited to the described exemplary embodiments . instead , it would be appreciated by those skilled in the art that changes may be made in these example embodiments of the present inventive concept without departing from the principles and spirit of the disclosure , the scope of which is defined in the claims and their equivalents .