Precise Control of Copper-Localized Surface Plasmon Resonance in the Near Infrared Region for Enhancement of Up-Conversion Luminescence

: The surface plasmon resonance of copper in the near infrared region provides a novel method for enhancement of up-conversion luminescence compared to using gold and silver, as the former grants signiﬁcant cost savings. In this study, we made a ﬂat Cu ﬁlm covered TiO 2 to enhance the up-conversion ﬂuorescence intensity. The results show that the deposition of copper / TiO 2 dioxide nanocomposite ﬁlm prepared via spin-coating has no e ﬀ ect on the structure of NaGdF 4 :Er 3 + , Yb 3 + . The absorption wavelength of the copper ﬁlm moved from the original visible wavelength (~600 nm) range to the infrared wavelength after covering TiO 2 , and most obviously, the copper ﬁlm covered two layers of TiO 2 by about 16 nm; the peak of the absorption appeared at 835 nm due to the enhanced excitation ﬁeld. The behavior of the nanocomposite ﬁlm with NaGdF 4 :Er 3 + and Yb 3 + under 980 nm excitation was investigated; it provides a novel way for studying mental-enhanced ﬂuorescence. Besides, the peaks of the ﬂuorescence spectrum show di ﬀ erent emissions at 542 nm and 660 nm, respectively. The copper nanoparticles-covered TiO 2 layer can obviously enhance the ﬂuorescence intensity, and the maximum enhancement factors of emission of NaGdF 4 :Er 3 + and Yb 3 + nanoparticles are 3.1 and 1.9 on the nanocomposite ﬁlm, respectively. TiO 2 structure. This also illustrates that the localized surface plasmon resonance (LSPR) peak plays a role in luminescence enhancement of up-conversion nanoparticles. The SPR of the


Introduction
In the last decade, up-conversion fluorescence intensity has attracted widespread attention for improving optics for a variety of applications [1,2]. For example, detecting bioprobes for optical tracking [3], biological imaging [4], photodynamic therapy [5], 3D displays [6,7] and solar energy conversion [8]. For example, NaGdF 4 :Er, Yb is known as a popular material for up-conversion luminescence [9][10][11][12]. Compared to the conventional fluorescent materials, the up-conversion has a different process which can lower the energy of a photon to stimulate higher energy photons [13]. The up-conversion process occurs by absorbing 980 nm laser irradiation and then successively transfering the excitation energy to nearby co-doped activators (Ho 3+ , Er 3+ , Tm 3+ , etc.) [14]. The sensitizer Yb dopant ions can absorb 980 nm photons and then transfer them to an adjacent activator (Er), which emits luminescence with a short wavelength. The wavelength of up-conversion emissions can be tuned in the ultraviolet, visible and near-infrared regions [15][16][17]. Subsequently,

Preparation of Substrate
The glass quartz plate used in this work was 1 mm in thickness; the length and width were 1.5 cm respectively. Before fabrication, the quartz plate was ultrasonically-cleaned in acetone and alcohol at room temperature for 30 min, and then washed in ultrapure water. When dried in slowing nitrogen, the glass sheet was degassed in a rapid annealing furnace at 600 • C for 15 min under a 5 Pa vacuum.

Sample Fabrication
Copper deposition was performed by magnetron sputtering with a deposition rate of 1 nm/s and an ionization current of 15 mA under a 10 Pa Ar atmosphere. In the study of surface topography, the copper film is deposited by precisely controlling the deposition time. In the annealing process, the samples were heated from the ambient (~25 • C) to the target temperature (900 • C) with a ramp rate of 80 • C·s −1 under N 2 atmosphere. The temperature was raised to 900 • C with an annealing duration of 1800 s to guarantee the sufficient surface diffusion. We used titanium butoxide (0.34 g) and 2-methoxyethanol (10 mL) in the process of making the titanium dioxide precursor solution and mixed the solution thoroughly to keep the solution stable. The mixed solution appears a faint yellow color and can remain stable at all times. Deposition of TiO 2 film was achieved by spin-coating at 3000 rpm, and then the sample was post-annealed at 550 • C with the annealing time of 3600 s. For the process of making up-conversion materials, we added 2 mL of methanol into GdCl 3 ·6H 2 O (0.289 g, 0.78 mmol), YbCl 3 ·6H 2 O (0.074 g, 0.2 mmol) and ErCl 3 ·6H 2 O (0.0076 g, 0.02 mmol) in a three-necked flask and ultrasonically mixed the solution. As the same time, oleic acid (8 mL) and octadecene (12 mL) were added to the flask. Evacuation is required before and during heating to remove oxygen from the flask and methanol from the solution. We used gradient heating from the ambient temperature (~25 • C) to 150 • C to ensure the nanoparticles' size is uniform and hold for 30 min at 70, 110 and 150 • C, respectively. Then, we used the room temperature cooling method to reduce the temperature to 50 • C for adding NaOH (0.1 g, 2.5 mmol) and NH 4 F (0.148 g, 4 mmol). The mixed solution was heated to 300 • C for half an hour and cooled to room temperature. Deposition of the up-conversion material film was achieved by spin-coating with the revolutions per minute of 2000. One consideration is to keep the material on the sample as much as possible, and the other is to make the film more uniform.

Characterization
The morphologies of Cu structure and up-conversion materials were characterized by scanning electron microscopy (SEM), transmission electron microscopy (TEM), micro-spectrophotometer, fluorescence detection equipment (FLS-1000), X-ray diffraction (XRD) and the photo-induced force microscope (PiFM). Topographies of the surfaces of Cu films were detected using PiFM from Molecular Vista, Inc. (San Jose, CA, USA). Micrographs of Cu films and coper nanoparticles with different thickness TiO 2 were detected using a FEG 650 SEM (Carl Zeiss SMT, Oberkochen, Germany). Absorbances of copper and copper with TiO 2 were characterized by a CRAIC 20/30 PVTM microspectrophotometer (CRAIC, San Dimas, CA, USA). Transmission electron microscopy (TEM) images of NaGdF 4 :Er 3+ , Yb 3+ nanoparticles were observed using a JEOL 2100 transmission electron microscope (JEOL, Tokyo, Japan). The XRD pattern was obtained by an X-ray diffractometer (Bruker D8 Advance, Bruker, Germany) with the scanning speed of 2 • /min. The up-conversion spectra of NaGdF 4 :Er 3+ , Yb 3+ were obtained with a FLS-1000 spectrophotometer (Edinburgh Inc., Livingston, UK) upon 980 nm excitation. Figure 1 shows the surface topography of copper nanoparticles on quartz glass at the annealing temperature of 900 • C with different Cu deposition times, and the diameter distribution histograms of copper nanoparticles are shown. The detailed morphology of Cu nanostructures is characterized by the atomic force microscope (AFM) in Figure 1a and scanning electron microscope (SEM) in Figure 1c-f. Figure 1a shows the AFM topography image of the copper nanoparticles. It is obvious that the height difference of the copper nanoparticles is about 73.6 nm in the AFM image, which illustrates that the Cu film was stimulated by nanoparticle formation at the annealing temperature. The yellow areas in Figure 1a represent nanoparticles with higher protrusions. Corresponding to the 3D image in Figure 1b, the results show a certain distance between the nanoparticles and show island-like shapes. As the same time, Cu nanoparticles fabricated with different deposition times were studied by SEM. It is obvious that the samples at different deposition times have different nanoparticle sizes. The size of nanoparticles distributes between 40 and 220 nm, as evidenced by the histograms in Figure 1g-j. Additionally, it can also be seen that the particle size distribution conforms to the normal distribution, and the calculated average sizes of nanoparticles with different deposition times are 53, 62, 100 and 120 nm, respectively. The cause of the differing sizes of nanoparticles may be explained by the following mechanism. When the copper deposition time is fixed and the heating temperature is 900 • C, it is generally agreed that the film is split into nanoparticles [37]. The process of forming a Cu nanostructure from a uniform Cu film can be explained based on solid state dewetting (SSD) [38][39][40]. As the deposition temperature was near the ambient (~25 • C), the as-deposited copper films have defects and vacancies which can offer favor sites for the high temperature nucleation. When sufficient energy is applied, vacancies can further develop on the surface of the Cu film. As the temperature further increases, the voids will grow as the surface diffusion of copper atoms increases [37]. As with the influence of the heating temperature of 900 • C, the degree of aggregation of the surrounding nanoparticles changes with the effect of Ostwald ripening [41,42]. Similarly, the shape of the nanoparticles also shows a different trend. As the deposition time increases, the shape of the copper nanoparticles gradually changed from spherical to irregular [37].

Results and Discussion
The SEM image of copper nanoparticles and the corresponding elemental mappings by EDS are shown in Figure 2. Si, O and Cu were observed in the sample, and the peaks of Si, O, Cu and Pt can be found in the EDS spectra. Since the sample was fabricated directly on the quartz substrate, the measured Si and O contents account for most of the color observed in Figure 2c,d. Before testing, we sputtered Pt with a nanoparticle size of 20 nm on copper nanoparticles to increase the conductivity of the sample and observe nanoparticle topography from charge accumulation at higher magnifications. From Figure 2a to Figure 2b, the amount of copper deposition increased and the proportion of the Cu element increased. It can be seen in Figure 2a that the time of sputtering for copper was less than it was the Figure 2b, and the Cu in Figure 2a accounts for 5.54%. The longer sputtering time evidenced by the proportion of Cu accounts for 9.35%. This also proves that the copper nanoparticles remaining on the substrate increase with increasing deposition time. The blue dots in Figure 2c,d show the magnification of copper nanoparticles, which also corresponds to the SEM image. The island-like distribution is also confirmed by Figure 2c,d's copper distribution caused by the SSD growth mechanism [41,42]. The SEM image of copper nanoparticles and the corresponding elemental mappings by EDS are shown in Figure 2. Si, O and Cu were observed in the sample, and the peaks of Si, O, Cu and Pt can be found in the EDS spectra. Since the sample was fabricated directly on the quartz substrate, the measured Si and O contents account for most of the color observed in Figure 2c,d. Before testing, we sputtered Pt with a nanoparticle size of 20 nm on copper nanoparticles to increase the conductivity of the sample and observe nanoparticle topography from charge accumulation at higher magnifications. From Figure 2a to 2b, the amount of copper deposition increased and the proportion of the Cu element increased. It can be seen in Figure 2a that the time of sputtering for copper was less than it was the Figure 2b, and the Cu in Figure 2a accounts for 5.54%. The longer sputtering time evidenced by the proportion of Cu accounts for 9.35%. This also proves that the copper nanoparticles remaining on the substrate increase with increasing deposition time. The blue dots in Figure 2c,d show the magnification of copper nanoparticles, which also corresponds to the SEM image. The island-like distribution is also confirmed by Figure 2c,d's copper distribution caused by the SSD growth mechanism [41,42]. Furthermore, we studied the SEM side-views of copper nanoparticles coated with TiO2. The TiO2 layers were deposited using spin-coating and then annealed at 550 °C under ambient air for 1 h. The schematic illustration of the copper nanoparticles covered with TiO2 can be seen in Figure 3a; it is obvious that the structure is similar to the physical model we expected to build, as shown in Figure  3b-d. The arrows point exactly to the copper nanoparticles and TiO2 films we synthesized, respectively. Thus, we can see that the copper nanoparticles are also island-like when they are covered with oxides, and the oxide coating was made on the copper nanoparticles with layers of about 40 nm in thickness (Figure 3d). Figure 3c,d shows different sizes of copper nanoparticles covered in TiO2 between 119 and 155 nm thick. The presence of oxide can also be seen in the divided Furthermore, we studied the SEM side-views of copper nanoparticles coated with TiO 2 . The TiO 2 layers were deposited using spin-coating and then annealed at 550 • C under ambient air for 1 h. The schematic illustration of the copper nanoparticles covered with TiO 2 can be seen in Figure 3a; it is obvious that the structure is similar to the physical model we expected to build, as shown in Figure 3b-d. The arrows point exactly to the copper nanoparticles and TiO 2 films we synthesized, respectively. Thus, we can see that the copper nanoparticles are also island-like when they are covered with oxides, and the oxide coating was made on the copper nanoparticles with layers of about 40 nm in thickness (Figure 3d). Figure 3c,d shows different sizes of copper nanoparticles covered in TiO 2 between 119 and 155 nm thick. The presence of oxide can also be seen in the divided areas between the copper nanoparticles, which shows that the uniformity of the film is perfect when spin-coating. The copper nanoparticles are tightly wrapped by the titanium dioxide, which can change the LSPR [1,43] of the metal nanoparticles. After measuring the structure by SEM and AFM, the absorption of the material structure was also investigated to show the absorbance change.
s. Furthermore, we studied the SEM side-views of copper nanoparticles coated with TiO2. The TiO2 layers were deposited using spin-coating and then annealed at 550 °C under ambient air for 1 h. The schematic illustration of the copper nanoparticles covered with TiO2 can be seen in Figure 3a; it is obvious that the structure is similar to the physical model we expected to build, as shown in Figure  3b-d. The arrows point exactly to the copper nanoparticles and TiO2 films we synthesized, respectively. Thus, we can see that the copper nanoparticles are also island-like when they are covered with oxides, and the oxide coating was made on the copper nanoparticles with layers of about 40 nm in thickness (Figure 3d). Figure 3c,d shows different sizes of copper nanoparticles covered in TiO2 between 119 and 155 nm thick. The presence of oxide can also be seen in the divided areas between the copper nanoparticles, which shows that the uniformity of the film is perfect when spin-coating. The copper nanoparticles are tightly wrapped by the titanium dioxide, which can change the LSPR [1,43] of the metal nanoparticles. After measuring the structure by SEM and AFM, the absorption of the material structure was also investigated to show the absorbance change.    [44,45] of the copper nanoparticles varies from 570 nm to 580 nm. The absorption maximum of each sample corresponds to that of the surface plasmon band of the copper nanoparticles. With the increase of copper deposition time, the intensity of the absorption also increases and the absorption of copper nanoparticles has a 10 nm red shift due to the particle size increase with the time of copper deposition. At the same time, the absorption of copper nanoparticles covered by 1-layer or 2-layers TiO 2 is also studied in Figure 4. The absorption spectra of different samples exhibited the obvious absorption bands between 670 and 770 nm and 765 and 835 nm originating from the SPR [44,45] of the copper nanoparticles with TiO 2 , and the absorption spectra of TiO 2 appear at 330 nm. It is obvious that the second peak is the absorption of copper nanoparticles covered with TiO 2 , and the absorption peak of copper nanoparticles whether covered one layer or two layers of TiO 2 has an obvious red-shift compared to the absorption of pure copper nanoparticles. The absorption has maximum red shifts of 160 and 235 nm compared to the peak of pure copper nanoparticles appearing at about 600 nm, respectively. The reason for the red shift is mainly due to the size effect of copper nanoparticles [46]. Additionally, the metal nanoparticles significantly increase light absorption and produce a plasmon resonance frequency shift of the absorption peak. In the meantime, the red shift of absorption of copper nanoparticles covered in TiO 2 depends on the modulation of dielectric environment [47], and the absorption peak of copper nanoparticles has much more red shift compared to the isolated copper nanoparticles. Thus, the absorption peak position of the nanoparticles reached 835 nm from the original 570 nm. As the same time, it is obvious that the copper deposition time of 150 s covered in two layers of TiO 2 has a wider absorption band than the other samples. absorbance peak has a red shift when the surfaces of copper nanoparticles are covered in one or two layers TiO2. The biggest change of the absorption peak is from the original 580 nm to about 830 nm can be seen in Figure 5a. But the 180 s copper deposition covered 2 layers TiO2 does not perform as well as other samples and the maximum absorption appear at 750 nm. At the same time, the intensity of absorption is also one of important factors in terms of fluorescence enhancement. We can see that the intensity of the absorption peak showing a downward trend in Figure 5b. When the absorption peak position reaches the near infrared band, it must also ensure the absorption intensity. Thus, the time of 90 s, 110 s,150 s coper deposition covered TiO2 are selected samples to study the enhancement of fluorescence.   Figure 5 shows the change of absorbance peak position and absorbance peak position of copper nanoparticles covered by TiO 2 of different thickness. As the same time, we can obtain that the absorbance peak has a red shift when the surfaces of copper nanoparticles are covered in one or two layers TiO 2 . The biggest change of the absorption peak is from the original 580 nm to about 830 nm can be seen in Figure 5a. But the 180 s copper deposition covered 2 layers TiO 2 does not perform as well as other samples and the maximum absorption appear at 750 nm. At the same time, the intensity of absorption is also one of important factors in terms of fluorescence enhancement. We can see that the intensity of the absorption peak showing a downward trend in Figure 5b. When the absorption peak position reaches the near infrared band, it must also ensure the absorption intensity. Thus, the time of 90 s, 110 s, 150 s coper deposition covered TiO 2 are selected samples to study the enhancement of fluorescence. In the synthesis of the NaGdF4:Yb 3+ , Er 3+ nanoparticles, we adopted hydrothermal method. When the heating temperature was selected, the operation was carried out by heating between zones while maintaining a certain temperature for half an hour to keep the size of NaGdF4:Yb 3+ , Er 3+ nanoparticles uniform. As the same time, the size is typically ~9 nm in the TEM image and the size distribution can be seen in Figure 6a,b. The particles size varies from 6 to 12 nm and it fits to the normal distribution. Figure 6c shows the XRD patterns NaGdF4:Yb 3+ , Er 3+ nanoparticles. The diffraction peaks in Figure 6c at 29.6°, 42.7°, 53.4° match well with XRD peaks of the standard cards (JCPDS:27-0699) of NaGdF4:Yb 3+ , Er 3+ because of X-ray diffraction of the (1 0 1), (2 0 1) and (2 1 1) facets [48]. The spectrum of the measured sample is consistent with the standard card, indicating that the material formed a certain lattice structure which can be seen in Figure 6a. The up-conversion material was also spincoated on top of the copper nanoparticles and then the basic fluorescence test was performed after a In the synthesis of the NaGdF 4 :Yb 3+ , Er 3+ nanoparticles, we adopted hydrothermal method. When the heating temperature was selected, the operation was carried out by heating between zones while maintaining a certain temperature for half an hour to keep the size of NaGdF 4 :Yb 3+ , Er 3+ nanoparticles uniform. As the same time, the size is typically~9 nm in the TEM image and the size distribution can be seen in Figure 6a,b. The particles size varies from 6 to 12 nm and it fits to the normal distribution. Figure 6c shows the XRD patterns NaGdF 4 :Yb 3+ , Er 3+ nanoparticles. The diffraction peaks in Figure 6c at 29.6 • , 42.7 • , 53.4 • match well with XRD peaks of the standard cards (JCPDS:27-0699) of NaGdF 4 :Yb 3+ , Er 3+ because of X-ray diffraction of the (1 0 1), (2 0 1) and (2 1 1) facets [48]. The spectrum of the measured sample is consistent with the standard card, indicating that the material formed a certain lattice structure which can be seen in Figure 6a. The up-conversion material was also spin-coated on top of the copper nanoparticles and then the basic fluorescence test was performed after a simple curing process by drying at room temperature. During the fluorescence test, we selected samples of copper nanoparticles at different deposition times of 2-layer TiO2, and also performed a bare control. There are two obvious fluorescence emission peaks of the NaGdF4:Yb, Er nanoparticles: green emission at 542 nm and red emission at 660 nm in Figure 7a. The intensity of fluorescence measured directly on quartz glass is weak as the amount of up-conversion material left on the glass sheet by spin coating is very low, and there is a dramatic enhancement observed in the measured fluorescence when the up-conversion material spin-coating on the Cu/TiO2 structure. This also illustrates that the localized surface plasmon resonance (LSPR) peak plays a role in luminescence enhancement of up-conversion nanoparticles. The SPR of the Cu/TiO2 red shifted to 835 nm, matching well with the excitation wavelength, as can be seen in Figure  4. The ratio of different fluorescence emission is recorded in Figure 7b. It can be seen that as the time of copper deposition covered TiO2 increases, the maximum fluorescence ration overall increases gradually. Thus, with the LSPR peak is turned to 835 nm, the ratios of green and red emission can be about 3 and 2 times, respectively. The results show the LSPR with the excitation field can influence the up-conversion luminescence and then cause a strength enhancement of the local excitation field [35]. The NaGdF 4 can be known as the popular material for up-conversion luminescence and under 980 nm excitation [9], NaGdF 4 can have green and red emission doping Yb 3+ , Er 3+ . Figure 6d is the mechanism of up-conversion processes of NaGdF 4 :Yb 3+ , Er 3+ , Yb 3+ absorbs the energy of the 980 nm which the energy can transfers into Er 3+ and Er 3+ return to ground state from excited state [49]. Energy level schematic can be explained by the following theory. First, the electrons of Yb ions can change from 2 F 7/2 to 2 F 5/2 under the laser of 980 nm, which can influence the electrons of Er ions from 4 I 15/2 to 4 I 11/2 [35]. As the same time, a part of electrons changes from 4 I 11/2 to 4 I 13/2 by the non-radiative method on the surface of up-conversion nanoparticles. Then adjacent Yb ions can absorb electrons and influence the Er ions which can change the energy state of Er ions from 4 I 11/2 to 4 F 7/2 or from 4 I 13/2 to 4 F 9/2 . And on the 4 F 7/2 energy level of Er ions to 2 H 11/2 and 4 S 3/2 by the method of non-radiative which can cause the green emission of 2 H 11/2 → 4 I 15/2 and 4 S 3/2 → 4 I 15/2 . As the same time, on the 4 F 9/2 energy level of Er ions can radiate to the ground state which generate 4 F 9/2 → 4 I 15/2 transitions [36,50]. Thus, the green emission from 515 nm to 530 nm and 530 nm to 550 nm is determined by 2 H 11/2 → 4 I 15/2 and 4 S 3/2 → 4 I 15/2 transitions. The red emission is attributed to the 4 F 9/2 → 4 I 15/2 transitions. Here in this work, the 542 nm and 660 nm emission are our targeted.
During the fluorescence test, we selected samples of copper nanoparticles at different deposition times of 2-layer TiO 2 , and also performed a bare control. There are two obvious fluorescence emission peaks of the NaGdF 4 :Yb, Er nanoparticles: green emission at 542 nm and red emission at 660 nm in Figure 7a. The intensity of fluorescence measured directly on quartz glass is weak as the amount of up-conversion material left on the glass sheet by spin coating is very low, and there is a dramatic enhancement observed in the measured fluorescence when the up-conversion material spin-coating on the Cu/TiO 2 structure. This also illustrates that the localized surface plasmon resonance (LSPR) peak plays a role in luminescence enhancement of up-conversion nanoparticles. The SPR of the Cu/TiO 2 red shifted to 835 nm, matching well with the excitation wavelength, as can be seen in Figure 4. The ratio of different fluorescence emission is recorded in Figure 7b. It can be seen that as the time of copper deposition covered TiO 2 increases, the maximum fluorescence ration overall increases gradually. Thus, with the LSPR peak is turned to 835 nm, the ratios of green and red emission can be about 3 and 2 times, respectively. The results show the LSPR with the excitation field can influence the up-conversion luminescence and then cause a strength enhancement of the local excitation field [35].
peaks of the NaGdF4:Yb, Er nanoparticles: green emission at 542 nm and red emission at 660 nm in Figure 7a. The intensity of fluorescence measured directly on quartz glass is weak as the amount of up-conversion material left on the glass sheet by spin coating is very low, and there is a dramatic enhancement observed in the measured fluorescence when the up-conversion material spin-coating on the Cu/TiO2 structure. This also illustrates that the localized surface plasmon resonance (LSPR) peak plays a role in luminescence enhancement of up-conversion nanoparticles. The SPR of the Cu/TiO2 red shifted to 835 nm, matching well with the excitation wavelength, as can be seen in Figure  4. The ratio of different fluorescence emission is recorded in Figure 7b. It can be seen that as the time of copper deposition covered TiO2 increases, the maximum fluorescence ration overall increases gradually. Thus, with the LSPR peak is turned to 835 nm, the ratios of green and red emission can be about 3 and 2 times, respectively. The results show the LSPR with the excitation field can influence the up-conversion luminescence and then cause a strength enhancement of the local excitation field [35].

Conclusions
In this work, the Cu/TiO2 hybrid film was successfully synthesized which the copper nanoparticles prepared by sputtering and the TiO2 film used by spin-coating. The evolutions of the

Conclusions
In this work, the Cu/TiO 2 hybrid film was successfully synthesized which the copper nanoparticles prepared by sputtering and the TiO 2 film used by spin-coating. The evolutions of the morphological and optical properties of copper nanoparticles and TiO 2 were studied. We concluded that the maximum absorption of the Cu/TiO 2 hybrid film appeared at about 835 nm, and it redshift about 235 nm more than the absorption of pure copper nanoparticles. The changing of absorption is mainly related to the different thickness of TiO 2 on the copper nanoparticles. As the same time, the position of the maximum absorbance of hybrid film matches with the excitation of the up-conversion. Thus, the fluorescence of up-conversion material enhanced and the maximum ratios of intensity of fluorescence at 542 nm and 650 nm were 3.1 and 1.9, respectively. The enhanced fluorescence was related to the surface plasmon which was mainly from the excitation field enhancement due to the modulation of dielectric environment by changing the TiO 2 layer's thickness. Because of this simple and feasible way to enhance the up-conversion fluorescence, the fabrication of Cu/TiO 2 film is expected to be used in bioprobes for optical tracking, solar cells effective for absorbed infrared light and anti-counterfeiting technology.