Tuning Multicolor Emission of Manganese-Activated Gallogermanate Nanophosphors by Regulating Mn Ions Occupying Sites for Multiple Anti-Counterfeiting Application

The ability to manipulate the luminescent color, intensity and long lifetime of nanophosphors is important for anti-counterfeiting applications. Unfortunately, persistent luminescence materials with multimode luminescent features have rarely been reported, even though they are expected to be highly desirable in sophisticated anti-counterfeiting. Here, the luminescence properties of Zn3Ga2GeO8:Mn phosphors were tuned by using different preparation approaches, including a hydrothermal method and solid-state reaction approach combining with non-equivalent ion doping strategy. As a result, Mn-activated Zn3Ga2GeO8 phosphors synthesized by a hydrothermal method demonstrate an enhanced red photoluminescence at 701 nm and a strong green luminescence with persistent luminescence and photostimulated luminescence at 540 nm. While Mn-activated Zn3Ga2GeO8 phosphors synthesized by solid-state reactions combined with a hetero-valent doping approach only exhibit an enhanced single-band red emission. Keeping the synthetic method unchanged, the substitution of hetero-valent dopant ion Li+ into different sites is valid for spectral fine-tuning. A spectral tuning mechanism is also proposed. Mn-activated Zn3Ga2GeO8 phosphors synthesized by a hydrothermal approach with multimodal luminescence is especially suitable for multiple anti-counterfeiting, multicolor display and other potential applications.


Introduction
The ability to tune the luminescent color of materials is essential for various applications, such as anti-counterfeiting, three-dimensional displays, information coding, bioimaging, optoelectronic devices and luminescent labeling [1][2][3]. Conventional approaches involve utilizing specially designed organic dyes or quantum dots upon ultraviolet or blue light excitation, where the emission color is modulated by tuning the wavelengths or the power density of excitation light [4,5], thus posing limitations in the resolution of imaging due to auto-fluorescence. Persistent luminescence (PersL) phosphors, which can emit luminescence lasting for hours after the stoppage of the excitation light [6], are particularly suitable for such imaging applications as they emit no background fluorescence [7,8].
The transition metal Mn with the multiple oxidation states, e.g., +2, +3 and +4, provides an opportunity for multi-color emission [9]. In recent years, Mn-doped ZnGa 2 O 4 microcrystals with unique luminescence features have attracted much attention because a ZnGa 2 O 4 host has two kinds of stable chemical coordination structure, including Ga 3+ sites with octahedral coordination and Zn 2+ sites with tetrahedral coordination [10]. Generally, a Mn 2+ activation center occupying the tetrahedral-coordinated sites shows a green emission with long PersL, while a Mn 4+ activation center with an octahedral-coordinated

Sample Preparation
Zn 3 Li 0.4 Ga 1.6 GeO 8 :0.25% Mn phosphor was synthesized by using a hydrothermal method [8,11]. The synthesis procedure is described below. GeO 2 powders were dissolved in a sodium hydroxide solution to achieve 0.5 M Na 2 GeO 3 solution. Then, 3.0 mL 0.5 M Zn(NO 3 ) 2 , 0.0375 mL 0.1 M Mn(NO 3 ) 2 and 0.3 mL concentrated HNO 3 were together added slowly into 10 mL deionized water and then violently stirred. Subsequently, 0.4 mL 0.5 M LiNO 3 , 1.6 mL 0.5 M Ga(NO 3 ) 3 and 1.1 mL 0.5 M Na 2 GeO 3 were added to the above solution. After the solution was stirred vigorously for 1 h, concentrated ammonium hydroxide was added into the mixture of precursor solution to tune the pH of the mixed solution to 7.5, and then the mixed solution was stirred vigorously for 1 h at ambient temperature. The final colloid was transferred into a 50 mL polytetrafluoroethylene reactor, which was then placed in an oven and heated at 220 • C for 10 h. Finally, the resulting suspension was centrifuged and washed 3 times using deionized water. The collected products were dried at 70 • C, and were then annealed in a chamber-type electric resistance furnace in air at 1100 • C for 2 h.
The synthesis procedure of Zn 2. 4 Li 0.6 Ga 2 GeO 8 :Mn phosphors by hydrothermal method was similar to that of Zn 3 Li 0.4 Ga 1.6 GeO 8 :0.25% Mn only via 0.6 mL 0.5 M LiNO 3 substituting for 20% Zn(NO 3 ) 2 . According to our previous study [8,11], 20% Li substitution is an optimal doping concentration. Zn 3 Ga 2 GeO 8 :0.25% Mn phosphors were prepared via a solid-state reaction approach using ZnO, Ga 2 O 3 , GeO 2 , and MnO as raw materials [12]. Raw materials were weighted on the basis of the formula of Zn 3 Ga 2 GeO 8 :0.25%Mn and finely mixed in an agate. All the ground powders were then pre-calcined at 900 • C for 2 h. Subsequently, the pre-calcined products were sintered at 1100 • C for 2 h and then cooled down to ambient temperature.
The synthesis procedure of Zn 2. 4 Li 0.6 Ga 2 GeO 8 :Mn phosphor synthesized by a solid state reaction approach was similar to that of Zn 3 Ga 2 GeO 8 :0.25% Mn only via Li substituting for 20% ZnO.

Inks Preparation and Anti-Counterfeiting Patterns
Luminescence inks were fabricated based on a modified approach [13]. Typically, the prepared phosphors were dispersed into a mixed solution of 1.0 mL hydrochloric acid (0.2 mol/L) and 1.0 mL anhydrous C 2 H 5 OH, and then the mixed solution was centrifuged and washed with deionized water and anhydrous C 2 H 5 OH several times. Finally, the powders were mixed with PVA aqueous solution in a ratio of 1:1 to fabricate luminescent anti-counterfeiting inks. The luminescent patterns printed on the paper were achieved using screen printing method.

Characterization
A D/Max2400 X-ray diffractometer (XRD, Rigaku, Japan) with Cu Kα (40 kV, 100 mA) irradiation (λ = 1.5406 Å) was employed to characterize the crystal structures of phosphors. The shape and size of phosphors were characterized using a ZEISS Gemini 500 scanning electron microscopy (SEM) (Oberkochen, Germany). A spectrometer (PHI 5600ci ESCA, PerkinElmer, Waltham, MA, USA) with monochromatized Al K radiation was used to measure the X-ray photoelectron spectra (XPS) at room temperature. Thermoluminescence (TL) curves of products were measured using a TOSL-3DS TL spectrometer (Guangzhou, China) with a temperature range from 25 to 500 • C and a heating rate of 2 • C/s. A Horiba PTI QuantaMaster 8000 spectrofluorometer (Burlington, ON, Canada) equipped with a 75 W xenon lamp was used to study the optical properties of products. In addition, besides the xenon lamp as an irradiation source, two UV lamps (a 4-W 254 nm and a 5-W 365 nm) and two NIR laser diodes (0-2 W 808 nm and 0-5 W 980 nm) were also employed as excitation sources. When NIR lasers were used for irradiating the anti-counterfeiting patterns, the entire anti-counterfeiting pattern was programmatically scanned by the laser beam at a rate of 3 times per min. A Nikon EOS 60D camera (Tokyo, Japan) was used to take photographs of anti-counterfeiting patterns with suitable optical filters.  Figure 1c, are the compounds of cubic ZnGa 2 O 4 (JCPDS No. 01-071-0843) with an Fd3m space group and rhombohedral Zn 2 GeO 4 (JCPDS No. 04-007-5691) with an R3 space group [6,14,15]. While the XRD patterns of Zn 2.4 Li 0.6 Ga 2 GeO 8 :Mn prepared by a solid-state reaction method in Figure 1d demonstrate spinel-structured solid solutions of ZnGa 2 O 4 and Zn 2 GeO 4 [16,17]. It is reported that Zn 3 Ga 2 GeO 8 solid solutions are formed by Ge 4+ substituting for Ga 3+ into a ZnGa 2 O 4 lattice, where excessive Zn 2+ is necessary to counterbalance the charge disequilibrium [6,17]. It was observed that a solid solution is easier to form when Li replaces Ga, as shown in Figure 1b, which corresponds to a reduced Ga to Zn ratio but an excess of Zn in the hydrothermal reaction process, relative to Li + replacing Zn 2+ (Figure 1c). With the addition of Li + , substituting for Zn 2+ (Figure 1d) in the solid-state reaction, the phase purity becomes higher relative to the results shown in Figure 1e, indicating that the Ge 4+ ions (53 pm for ionic radius) enter into octahedral Ga 3+ (62 pm for ionic radius) sites [17] and Li + (76 pm for ionic radius) is substituted for Zn 2+ (74 pm for ionic radius) sites [18] for charge compensation [19]. The results of XRD patterns indicate that different preparation approaches and non-equivalent doping strategies have a great influence on the crystal structure of the Zn 3 Ga 2 GeO 8 phosphor. pm for ionic radius) sites [17] and Li + (76 pm for ionic radius) is substituted for Zn 2+ (74 pm for ionic radius) sites [18] for charge compensation [19]. The results of XRD patterns indicate that different preparation approaches and non-equivalent doping strategies have a great influence on the crystal structure of the Zn3Ga2GeO8 phosphor.  that there is no difference in element types and element distribution in these two kinds of samples. Clearly, the preparation method is one of the key factors that determines the crystal structure and morphology of these phosphors. The reasons for the differences in the crystal phase structure of the samples prepared by different methods could be complex. In a solid-state reaction system, a high temperature facilitates GeO2 volatilization, leading to the formation of a solid solution. On the other hand, hydrothermal conditions may also be beneficial for the coexistence of rhombohedral Zn2GeO4 and cubic ZnGa2O4.   that there is no difference in element types and element distribution in these two kinds of samples. Clearly, the preparation method is one of the key factors that determines the crystal structure and morphology of these phosphors. The reasons for the differences in the crystal phase structure of the samples prepared by different methods could be complex. In a solid-state reaction system, a high temperature facilitates GeO 2 volatilization, leading to the formation of a solid solution. On the other hand, hydrothermal conditions may also be beneficial for the coexistence of rhombohedral Zn 2 GeO 4 and cubic ZnGa 2 O 4 .

Results and Discussion
All phosphors used in the experiments were annealed at 1100 • C due to their more distinctive luminescence features than their as-synthesized counterparts. Manganeseactivated gallogermanate-based phosphors synthesized by a hydrothermal approach via Li replacing 20% Ga 3+ are referred to as Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn phosphor, and those synthesized via Li replacing 20% Zn 2+ are referred to as Zn 2. 4 Li 0.6 Ga 2 GeO 8 :Mn phosphor. The Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn phosphor was investigated first, and Figure 3 illustrates its excited wavelength-dependent luminescence features. Under a 254 nm UV lamp excitation, a bluewhite broad-band spectrum in the range of 400-750 nm was achieved ( Figure 3a) and could be ascribed to the transitions of matrix defect levels. When the excitation wavelength was switched to 357 nm, the strong red emission of Mn 4+ ions from 2 E→ 4 A 2 (peaking at 701 nm) transitions could be obtained, accompanied with a weak green emission (540 nm) from 4 T 1 (4G)→ 6 A 1 (6S) transitions of Mn 2+ ions ( Figure 3a) [20,21]. Finally, when the sample was irradiated with blue visible light at 467 nm, only a pure-red single band at 650-800 nm from 2 E→ 4 A 2 of Mn 4+ was observed ( Figure 3a) [21]. PL excitation (PLE) spectrum monitoring at 540 nm shows a typical Mn 2+ -O 2− charge transfer band (CTB) centered at 283 nm ( Figure 3b) [22]. PLE spectrum monitoring at 701 nm shows two broad bands (excitation band I at 200−400 nm and excitation band II at 400-620 nm) peaking at 357 nm and 467 nm in Figure 3b. The excitation band I peaking at 357 nm originated from 4 A 2 → 4 T 1 , while excitation band II peaking at 467 nm was assigned to the 4 A 2 → 4 T 2 transitions of Mn 4+ ions [23]. The profile and peak position on the PLE spectra monitored at 701 and 540 nm are different, which indicates that red and green emissions come from different Mn emission centers. These spectra indicate that Li + replacing Ga 3+ provides an opportunity for Mn to occupy the octahedral Ga 3+ sites. As a result, in Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn crystals, Mn occupies two kinds of positions: one is a tetrahedral Zn site, and the other is octahedral Ga site. These results are consistent with the above XRD analysis. All phosphors used in the experiments were annealed at 1100 °C due to their more distinctive luminescence features than their as-synthesized counterparts. Manganese-activated gallogermanate-based phosphors synthesized by a hydrothermal approach via Li replacing 20% Ga 3+ are referred to as Zn3Li0.4Ga1.6GeO8:Mn phosphor, and those synthesized via Li replacing 20% Zn 2+ are referred to as Zn2.4Li0.6Ga2GeO8:Mn phosphor. The Zn3Li0.4Ga1.6GeO8:Mn phosphor was investigated first, and Figure 3 illustrates its excited wavelength-dependent luminescence features. Under a 254 nm UV lamp excitation, a blue-white broad-band spectrum in the range of 400-750 nm was achieved ( Figure 3a) and could be ascribed to the transitions of matrix defect levels. When the excitation wavelength was switched to 357 nm, the strong red emission of Mn 4+ ions from 2 E→ 4 A2 (peaking at 701 nm) transitions could be obtained, accompanied with a weak green emission (540 nm) from 4 T1(4G)→ 6 A1(6S) transitions of Mn 2+ ions (Figure 3a) [20,21]. Finally, when the sample was irradiated with blue visible light at 467 nm, only a pure-red single band at 650-800 nm from 2 E→ 4 A2 of Mn 4+ was observed (Figure 3a) [21]. PL excitation (PLE) spectrum monitoring at 540 nm shows a typical Mn 2+ -O 2− charge transfer band (CTB) centered at 283 nm (Figure 3b) [22]. PLE spectrum monitoring at 701 nm shows two broad bands (excitation band I at 200−400 nm and excitation band II at 400-620 nm) peaking at 357 nm and 467 nm in Figure 3b. The excitation band I peaking at 357 nm originated from 4 A2→ 4 T1, while excitation band II peaking at 467 nm was assigned to the 4 A2→ 4 T2 transitions of Mn 4+ ions [23]. The profile and peak position on the PLE spectra monitored at 701  Figure 3c, which may originate from the pre-irradiated wavelength-dependent trapping and detrapping [24]. Aside from PL and PersL, the UV pre-irradiated Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn phosphor also exhibited superior PSL capabilities, peaking at 540 nm and 670 nm (Figure 3a) under the illumination of a 980 nm laser diode, which is consistent with previous reports [25,26]. We still found that the PL and PSL emission spectra were slightly different (Figure 3a). We know that green luminescence (with PersL feature) and red luminescence (without PersL characteristics) originate from the Mn 2+ and Mn 4+ luminescent centers, respectively. Theoretically, red PSL should not be observed due to no red PersL. Surprisingly, we could still observe red luminescence, but no green luminescence was achieved when we emptied the traps of Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn phosphor and then the sample was excited under 980 nm, suggesting that the red fluorescence may be derived from the upconversion fluorescence of Mn ions [27]. These results show that red and green PL with different luminescent features should derive from the luminescent center with different coordination environments. In addition, the Zn3Li0.4Ga1.6GeO8:Mn phosphor can demonstrate superior green PersL properties. After the removal of UV radiation, the green luminescence (monitored at 540 nm) of the Zn3Li0.4Ga1.6GeO8:Mn phosphor shows a long PersL signal (Figure 3c). A PersL spectrum achieved at 7 s of the decay is shown in the inset of Figure 3b. The similar PersL profile indicated that the PersL could be attributed to the Mn 2+ ions. From Figure  3c, it is evident that Zn3Li0.4Ga1.6GeO8:Mn phosphor exhibited a good green PersL. Moreover, the excitation wavelength-dependent PersL duration is shown in Figure 3c, which may originate from the pre-irradiated wavelength-dependent trapping and detrapping [24]. Aside from PL and PersL, the UV pre-irradiated Zn3Li0.4Ga1.6GeO8:Mn phosphor also exhibited superior PSL capabilities, peaking at 540 nm and 670 nm (Figure 3a) under the illumination of a 980 nm laser diode, which is consistent with previous reports [25,26]. We still found that the PL and PSL emission spectra were slightly different (Figure 3a). We know that green luminescence (with PersL feature) and red luminescence (without PersL characteristics) originate from the Mn 2+ and Mn 4+ luminescent centers, respectively. Theoretically, red PSL should not be observed due to no red PersL. Surprisingly, we could still observe red luminescence, but no green luminescence was achieved when we emptied the traps of Zn3Li0.4Ga1.6GeO8:Mn phosphor and then the sample was excited under 980 nm, suggesting that the red fluorescence may be derived from the upconversion fluorescence of Mn ions [27]. These results show that red and green PL with different luminescent features should derive from the luminescent center with different coordination environments.
Interestingly, the fluorescent colors of Mn-activated Zn3Ga2GeO8 phosphor prepared by a hydrothermal approach could be further finely adjusted by substituting Zn 2+ with Li + to tune the occupancy rate of Mn ions in Zn 2+ and Ga 3+ sites. Figure 4 shows the luminescence characteristics of Zn2.4Li0.6Ga2GeO8:Mn phosphor prepared by a hydrothermal approach. As expected, the fluorescence emission color changed from green to yellow to red in response to the excitation wavelength (Figure 4a). Under excitation at 254 nm, the sample showed a broad-band emission spanning a range of 400-800 nm wavelength ( Figure  4a), which is similar to the emission of Zn3Li0.4Ga1.6GeO8:Mn phosphor. When the excitation wavelength was switched to 337 nm, the green emission (Figure 4a), which can be assigned to the 4 T1(4G)→ 6 A1(6S) transition of Mn 2+ , dominated the emission, accompanying the weak red emission peaking at 701 nm [26]. PLE spectrum monitored at 540 nm Interestingly, the fluorescent colors of Mn-activated Zn 3 Ga 2 GeO 8 phosphor prepared by a hydrothermal approach could be further finely adjusted by substituting Zn 2+ with Li + to tune the occupancy rate of Mn ions in Zn 2+ and Ga 3+ sites. Figure 4 shows the luminescence characteristics of Zn 2.4 Li 0.6 Ga 2 GeO 8 :Mn phosphor prepared by a hydrothermal approach. As expected, the fluorescence emission color changed from green to yellow to red in response to the excitation wavelength (Figure 4a). Under excitation at 254 nm, the sample showed a broad-band emission spanning a range of 400-800 nm wavelength (Figure 4a), which is similar to the emission of Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn phosphor. When the excitation wavelength was switched to 337 nm, the green emission (Figure 4a), which can be assigned to the 4 T 1 (4G)→ 6 A 1 (6S) transition of Mn 2+ , dominated the emission, accompanying the weak red emission peaking at 701 nm [26]. PLE spectrum monitored at 540 nm exhibited twin peaks in a 200-400 nm wavelength range (Figure 4b), which were assigned to the Mn 2+ -O 2− CTB and the 5d→5d transition of Mn 2+ with tetrahedral coordination [9,22]. Under the 413 nm excitation, the phosphors exhibited a narrowband red emission (Figure 4a) originating from the spin-forbidden 4 T 1 (4G)→ 6 A 1 (6S) transition of Mn 2+ in the strong octahedral crystal field, which is different from the deep red emission of Mn 4+ (Figure 3a strong octahedral crystal field, which is different from the deep red emission of Mn 4+ (Figure 3a) of Zn3Li0.4Ga1.6GeO8:Mn phosphor. The PLE spectrum monitored at 701 nm exhibited triplet peaks at 276, 413 and 575 nm (Figure 4b), which were assigned to the Mn 2+ -O 2− CTB (276 nm) and the 5d→5d Mn 2+ transition (413 and 575 nm) [24]. Aside from wavelength-dependent PL properties, the UV pre-irradiated Zn2.4Li0.6Ga2GeO8:Mn phosphor also showed excellent green PersL (Figure 4c) and green PSL (Figure 4a) capability under the 980 nm laser diode illumination. Zn2.4Li0.6Ga2GeO8:Mn and Zn3Ga2GeO8:Mn phosphors synthesized by solid-state reaction demonstrated completely different fluorescence characteristics. The PLE and PL spectra of these phosphors are illustrated in Figure 5. We found that Zn3Ga2GeO8:Mn phosphor exhibited a broad-band red emission at 650-800 nm from 2 E→ 4 A2 transition of Mn 4+ ions, accompanied with the weak green color broad-band emission at 500-600 nm from matrix defect in Figure 5a. Meanwhile, Zn2.4Li0.6Ga2GeO8:Mn phosphor demonstrates a broad-band pure-red emission at 650-800 nm upon the 365 nm excitation, indicating that Li doping turns Mn 4+ into the spin-allowed weak crystal field, leading to a broader red band emission. In addition, the perceptible color of luminescence from the two samples can be directly observed, as shown in the digital imaging signals (Figure 5b). Compared with the orange light of Zn3Ga2GeO8:Mn phosphors without Li, the Zn2.4Li0.6Ga2GeO8:Mn phosphor exhibits an enhanced pure-red emission from Mn 4+ ions at 701 nm. The profile and peak position of PLE spectra (Figure 5a) are similar to the PLE spectra monitored at 701 nm as shown in Figure 3b, which indicates that the broad-band red luminescence for three samples (including Zn2.4Li0.6Ga2GeO8:Mn and Zn3Ga2GeO8:Mn phosphors synthesized by solid-state reaction and Zn3Li0.4Ga1.6GeO8:Mn phosphor synthesized by hydrothermal approach) come from the same Mn 4+ emission centers. Comparing the spectral characteristics of the four samples, we found that the emission peak at 701 nm and their PLE spectra show the same spectral profile and position in the three samples (Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn synthesized by a hydrothermal approach; Zn 2.4 Li 0.6 Ga 2 GeO 8 :Mn and Zn 3 Ga 2 GeO 8 :Mn phosphors synthesized by solid-state reaction). Comparing the XRD patterns of the three samples, we can find that all three samples have the same spinel-structured solid solutions. Combined with the spectral features, the broad red emission bands peaking at 701 nm are easily ascribed to 2 E→ 4 A 2 transitions of Mn 4+ [28,29], which occupied octahedral sites in a spinel-structured solid solutions of ZnGa 2 O 4 and Zn 2 GeO 4 . While the emission spectrum peaking at 701 nm and its PLE spectrum of Zn 2.4 Li 0.6 Ga 2 GeO 8 :Mn synthesized by a hydrothermal approach (Figure 4a,b) are different from the other three samples. The spin-forbidden red narrowband emission peaking at 701 nm can be ascribed to the 4 T 1 (4G)→ 6 A 1 (6S) transitions of Mn 2+ , which occupied the strong octahedral crystal field [30,31]  Comparing the spectral characteristics of the four samples, we found that the emission peak at 701 nm and their PLE spectra show the same spectral profile and position in the three samples (Zn3Li0.4Ga1.6GeO8:Mn synthesized by a hydrothermal approach; Zn2.4Li0.6Ga2GeO8:Mn and Zn3Ga2GeO8:Mn phosphors synthesized by solid-state reaction). Comparing the XRD patterns of the three samples, we can find that all three samples have the same spinel-structured solid solutions. Combined with the spectral features, the broad red emission bands peaking at 701 nm are easily ascribed to 2 E→ 4 A2 transitions of Mn 4+ [28,29], which occupied octahedral sites in a spinel-structured solid solutions of ZnGa2O4 and Zn2GeO4. While the emission spectrum peaking at 701 nm and its PLE spectrum of Zn2.4Li0.6Ga2GeO8:Mn synthesized by a hydrothermal approach (Figure 4a,b) are different from the other three samples. The spin-forbidden red narrow-band emission peaking at 701 nm can be ascribed to the 4 T1(4G)→ 6 A1(6S) transitions of Mn 2+ , which occupied the strong octahedral crystal field [30,31] in the cubic phase ZnGa2O4 lattice. Similarly, green luminescence with PersL and PSL features can be observed only in Zn3Li0.4Ga1.6GeO8:Mn and Zn2.4Li0.6Ga2GeO8:Mn phosphors with a rhombohedral Zn2GeO4 phase synthesized by a hydrothermal approach, indicating that the rhombohedral Zn2GeO4 is a good matrix for generating green afterglow of Mn 2+ -occupied tetrahedral sites. The broad emission band (400-750 nm) from Zn3Li0.4Ga1.6GeO8:Mn and Zn2.4Li0.6Ga2GeO8:Mn phosphor synthesized by a hydrothermal approach could be assigned to matrix defects under a 254 nm UV lamp excitation, which can be further verified by the PL and PLE spectra of undoped Zn3Li0.4Ga1.6GeO8 phosphor, as shown in Figure 6a. As a result, the hydrothermal approach is an effective method for the preparation of afterglow phosphors. The stored energy of Zn3Li0.4Ga1.6GeO8:Mn and Zn2.4Li0.6Ga2GeO8:Mn PersL phosphors can also be triggered by heating, which helps to release the absorbed energy and provide insights into PersL mechanism. TL curves monitored at 540 nm are shown in Figure 6b. The TL curves for Zn3Li0.4Ga1.6GeO8:Mn ( Figure  6b, green curve) and Zn2.4Li0.6Ga2GeO8:Mn (Figure 6b, red curve) are similar and can be divided into two broad bands at 358 K and 376 K, and at 363 K and 423 K, respectively. These results indicate the presence of a shallow trap and deep trap in the two matrix materials, and the existence of the deep traps provides the conditions for generating PersL. Compared to Zn3Li0.4Ga1.6GeO8:Mn phosphor, the traps of Zn2.4Li0.6Ga2GeO8:Mn phosphor As a result, the hydrothermal approach is an effective method for the preparation of afterglow phosphors. The stored energy of Zn 3 Li 0.4 Ga 1.6 GeO 8 :Mn and Zn 2.4 Li0 .6 Ga 2 GeO 8 :Mn PersL phosphors can also be triggered by heating, which helps to release the absorbed energy and provide insights into PersL mechanism. TL curves monitored at 540 nm are shown in Figure 6b. The TL curves for Zn 3 Figure 7 [8,22,32,33]. 5 min illumination for Zn3Li0.4Ga1.6GeO8:Mn (green curve) and Zn2.4Li0.6Ga2GeO8:Mn phosphors (red curve) prepared by hydrothermal method.
As a result, the hydrothermal approach is an effective method for the preparation of afterglow phosphors. The stored energy of Zn3Li0.4Ga1.6GeO8:Mn and Zn2.4Li0.6Ga2GeO8:Mn PersL phosphors can also be triggered by heating, which helps to release the absorbed energy and provide insights into PersL mechanism. TL curves monitored at 540 nm are shown in Figure 6b. The TL curves for Zn3Li0.4Ga1.6GeO8:Mn ( Figure  6b, green curve) and Zn2.4Li0.6Ga2GeO8:Mn (Figure 6b, red curve) are similar and can be divided into two broad bands at 358 K and 376 K, and at 363 K and 423 K, respectively. These results indicate the presence of a shallow trap and deep trap in the two matrix materials, and the existence of the deep traps provides the conditions for generating PersL. Compared to Zn3Li0.4Ga1.6GeO8:Mn phosphor, the traps of Zn2.4Li0.6Ga2GeO8:Mn phosphor are deeper, which may explain why Zn2.4Li0.6Ga2GeO8:Mn phosphor has a long green afterglow duration. The possible luminescence mechanisms, including green PL, PersL and PSL from Mn 2+ , and the two red PL from Mn 2+ and Mn 4+ are proposed and shown in Figure  7 [8,22,32,33].  The luminescent emission color response to excitation wavelength and excitation power is convenient for various applications [8,34,35]. To verify the feasibility of the phosphors in the anti-counterfeiting fields, we used these phosphors as inks printed the table lamp patterns in Figure 8. Mn 2+ ions, resulting in green continuous fluorescence from 4 T1 (4G)→ 6 A1 (6S) (540 nm).
The luminescent emission color response to excitation wavelength and excitation power is convenient for various applications [8,34,35]. To verify the feasibility of the phosphors in the anti-counterfeiting fields, we used these phosphors as inks printed the table lamp patterns in Figure 8. Figure 8a depicts the schematic diagram of these patterns. The lampshade and bulb are printed with Zn3Li0.4Ga1.6GeO8:Mn and Zn2.4Li0.6Ga2GeO8:Mn phosphor synthesized by a hydrothermal approach, respectively. Upon the irradiation of 254 nm UV light, the lampshade became blue-white due to the color mixture of the Mn PL and the defect fluorescence of matrix [36] (Figure 8b), while the bulb became blue-green (Figure 8b). After the stoppage of excitation light, both the lampshade (dark green) and the bulb (bright green) emitted green PersL (Figure 8c), while upon the irradiation of 365 nm UV light, the lampshade and the bulb emitted bright red PL and green PL, respectively (Figure 8d). After the stoppage of UV excitation, these two patterns both showed green PersL colors with different saturations (Figure 8e). After these two patterns disappeared, the entire 'desk lamp' pattern was illuminated by a 980 nm laser diode; the lampshade and the bulb were lit again (Figure 8f), with the lampshade Upon the irradiation of 254 nm UV light, the lampshade became blue-white due to the color mixture of the Mn PL and the defect fluorescence of matrix [36] (Figure 8b), while the bulb became blue-green (Figure 8b). After the stoppage of excitation light, both the lampshade (dark green) and the bulb (bright green) emitted green PersL (Figure 8c), while upon the irradiation of 365 nm UV light, the lampshade and the bulb emitted bright red PL and green PL, respectively (Figure 8d). After the stoppage of UV excitation, these two patterns both showed green PersL colors with different saturations (Figure 8e). After these two patterns disappeared, the entire 'desk lamp' pattern was illuminated by a 980 nm laser diode; the lampshade and the bulb were lit again (Figure 8f), with the lampshade emitting a dark green color and the bulb emitting a yellow-green color (for a 980 nm illumination at 0.5 W), which is consistent with spectral characterization. Therefore, Mn-activated Zn 3 Ga 2 GeO 8 phosphors hold a promise for multi-chrome (green, yellow and red) and multi-mode (PL, PersL, and PSL) anti-counterfeiting applications [37][38][39]. In addition, the PSL and PL of nanomaterials can be used for photodynamic activation [40], dosimetry [41], thermometry [42] and solid-state lighting [43].
Additionally, we need to point out that, for practical applications, the possibility of the power of the laser diodes (2 and 5 W for the 808 nm and 980 nm lasers, respectively) to generate even secondary heating effects on the samples should be considered. It is true that NIR lasers, such as 808 nm or 980 nm lasers, have been widely used for photothermal therapy (PTT) [44][45][46]. However, for PTT, the materials have strong absorptions for NIR, but they do not have luminescence. So, the energy absorbed is released as heat, while in the luminescence materials, the absorbed energy is released as luminescence [47,48]; therefore, heating is not a critical issue, even though it is unavoidable. Heating is always an issue for many applications with NIR lasers.

Conclusions
In summary, manganese-activated gallium germanate phosphors were successfully synthesized in two approaches, including a high-temperature solid-state reaction ap-proach and a hydrothermal method. We found, for the first time, that these Mn-activated Zn 3 Ga 2 GeO 8 phosphors prepared by a hydrothermal method and solid-state reaction method have different crystal phase structures and spectral properties. The phosphors prepared by the hydrothermal method exhibited a double-peak emission, including green PL with a PersL feature and red PL without a PersL effect, due to simultaneously having two kinds of occupancy sites. While the Mn-activated Zn 3 Ga 2 GeO 8 phosphors prepared by a solid-state reaction method only exhibited red PL. In addition, Li + ions were selectively substituted for the tetrahedral Zn site or the octahedral Ga site, leading to green light emission at 540 nm ( 4 T 1 (G)→ 6 A 1 (S) transition of Mn 2+ ) with an afterglow and red light centered at 701 nm ( 2 E→ 4 A 2 transition of Mn 4+ ) in the absence of afterglow. Particularly, Mn-activated Zn 3 Ga 2 GeO 8 phosphors synthesized by a hydrothermal approach via Li + replacing the Zn 2+ or Ga 3+ sites exhibit dynamic and multicolor emissions as luminescence labels for multiple anti-counterfeiting, thus revealing the great potential of these phosphors in multicolor display, anti-forgery, and other potential applications.