the present invention is now described more fully hereinafter with reference to the accompanying drawings , in which preferred embodiments of the inventions are shown . this invention may , however , be embodied in many different forms and should not be construed as limited to the embodiments set forth herein . rather , the invention is defined by the following claims . in the drawings , the thicknesses of layers and regions are exaggerated for clarity . [ 0026 ] fig1 illustrates first embodiments of the ingan / ingan quantum well structure which can be used for the blue and green leds . referring now to fig1 layer 1 is the substrate which can be sapphire , silicon carbide ( sic ), zinc oxide ( zno ) or other substrates . layer 2 is the low - temperature buffer . layer 3 is the undoped gan or si - doped gan grown at around 1030 ° c ., doped at a concentration of 2 × 1017 cm − 3 to 9 × 1018 cm − 3 . layer 4 is the inxga1 − xn barrier wherein x ranges from 0 to 0 . 001 , grown at a temperature from 700 ° c . to 800 ° c . after the growth of layer 4 , tmin and ammonia were flowed to form “ seeds ” for the growth of indium rich qds at the same growth temperature of layer 4 . layer 5 is the inyga1 − yn quantum well , wherein y is greater than x , grown at the same temperature of layer 4 . layer 6 is another inxga1 − xn barrier grown at the same temperature of layer 4 . layer 7 is the gan cap grown in the range of 800 ° c . to 1100 ° c . the typical thickness for each layer is 200 μm to 500 μm for layer 1 , 20 nm to 40 nm for layer 2 , 1 μm to 4 μm for layer 3 , 2 nm to 10 nm for layer 4 , 2 nm to 4 nm for layer 5 , 2 nm to 10 nm for layer 6 , and 10 nm to 1000 nm for layer 7 . still continuing with the description of fig1 layer 1 may be any material suitable for the growth of gan , such as sapphire , sic , zno , and other alternatives . layer 2 , the low temperature buffer , can also be a multi - layered algan / gan buffer . layer 3 can be undoped gan , or gan that is si - doped to a concentration 2 × 1017 cm − 3 to 9 × 1018 cm − 3 , or gan that is mg - doped to a concentration 5 × 1017 cm − 3 to 3 × 1020 cm − 3 . layers 4 and 5 can be gan and / or algan instead of ingan . layer 7 , the high temperature cap , can also be algan . [ 0028 ] fig2 shows the photoluminescence at room temperature of the first group qw in the first embodiment . the wavelength of the emission is 488 nm , which is in the blue region . also note the narrow full width at half maxium ( fwhm ) of the luminescence which makes the blue color “ pure ” to the naked eye . this method can be readily used in the growth and fabrication of blue leds . [ 0029 ] fig3 shows the transmission electron microscopy ( tem ) picture of the sqw in the first embodiment . as can be seen clearly from the figure , the qds , which manifest themselves as the dark contrasts in tem picture , are located at the interface between layer 4 ( the ingan barrier ) and the layer 5 ( the well ). the interface between layer 4 and layer 5 is sharp . as previously mentioned , after the deposition of the ingan barrier , flowing tmin and ammonia provides “ seeds ” for the subsequent growth of these dots . the flow rate and duration of tmin are important for the formation of these dots ; a flow rate of less than 100 μmol / min and duration of 2 seconds to 5 seconds are preferred . these qds have higher indium content than the well with typical difference of in content from 10 % to 60 %, and they emit light with longer wavelengths . in this case , the 488 nm luminescence comes from these qds instead of from the well . referring now to fig4 layer 1 is the substrate , which is preferably sapphire , sic or zno ; layer 2 is the low - temperature buffer grown at about 450 ° c . to 600 ° c . ; layer 3 is the undoped gan or si - doped gan , grown at around 1030 ° c . ; layer 4 is a gan or ingan grown at the same temperature as the barrier and well ; layer 5 is a inxga1 − xn barrier , wherein x ranges from 0 . 01 to 0 . 1 grown at about 700 ° c . to 800 ° c . ; after the growth of layer 5 , tmin and ammonia were flowed to form “ seeds ” for the growth of indium rich qds ;, layer 6 is the inyga1 − yn quantum well where y is greater than x ; layer 7 is another inxga1 − xn barrier typically similar to layer 5 ; layer 8 is the gan cap grown at temperatures in the range of between 800 ° c . and 1030 ° c . still continuing with the description of fig4 layer 1 may be any material suitable for the growth of gan , such as sapphire , sic , zno , and other alternatives with thickness of about 200 μm to 500 μm . layer 2 , the low temperature buffer which is about 20 nm to 40 nm thick , can also be a multi - layered algan / gan buffer . layer 3 can be undoped gan , or si - doped gan to a concentration 2 × 1017 cm − 3 to 9 × 1018 cm − 3 , or mg doped gan to a concentration 5 × 1017 cm − 3 to 3 × 1020 cm − 3 , and its thickness ranges from 1 um to 4 um . layer 4 can be gan , ingan or algan grown at the same temperature as the barrier and well with the thickness of about 5 nm to 30 nm ; layer 5 and 6 can be gan instead of ingan . layer 8 , the 10 nm to 1000 nm thick cap , can also be algan . [ 0032 ] fig5 shows the photoluminescence of the sqw in the second embodiment at room temperature . the wavelength is 540 nm , which is in the green region . thus , the method of the present invention can be readily used in the growth and fabrication of green leds . the insertion of the layer 4 in fig4 is important to extending the luminescence from 488 nm to 540 nm . without being bound by any theory of the invention , it is thought that the low temperature gan layer ( layer 4 in fig4 ) partially relaxes the compressive strain between the ingan well and barrier . this relaxation of compressive strain can result in a red shift in the luminescence . relaxation of the compressive strain can also enhance the ingan phase separation according to kaprov &# 39 ; s [ mrs internet j nitride semicond . res . 3 , 16 ( 1998 ).] theory , in which compressive strain can suppress the ingan phase separation . the relatively rough surface of the low - temperature ( lt ) gan layer ( layer 4 in fig4 ) could help keep the impinging indium atoms , which come from the cracking of tmin precursor , on the surface for a longer time , thereby increasing the indium incorporation which will also result in red - shifting of the luminescence . various articles of the scientific periodical and / or patent literature are cited throughout this application . each of such articles is hereby incorporated by reference in its entirety and for all purposes by such citation .