Synthesis of uv-resistant and colorless polyimide films for optoelectrical applications

ABSTRACT Due to their excellent mechanical properties and intrinsic flexibility, polyimides (PIs) are promising candidates for optoelectrical applications under harsh conditions such as

flexible organic solar cells as well as flexible smart windows, etc. Much progress has been made on their optical transmittance; however, there remain significant concerns about their

environmental stability, particularly their UV resistance. Herein, 4 types of colorless polyimides (CPIs) with different molecular structures containing trifluoromethyl, ethers, or fluorenes

are carefully designed, and the dependence of their UV resistance on structures is explored systematically. It is found that the introduction of isopropylidene, ethers and fluorenes

effectively enhances the UV resistance of CPI and its initial performance (optical transparency, thermal stability, and toughness) simultaneously as a result of the subtle manipulation of

the conjugation structures. Specifically, the optimized polyimide film shows decent optical properties (\({T}_{550{\rm{nm}}}\) ~ 88%, yellowness index ~3.26), and thermal stability (\({T}_{5

\% }\) ~ 503 °C in N2 atmosphere, \({T}_{{\rm{g}}}\) ~ 312 °C). Moreover, after high-intensity UV irradiation, CPI not only maintains over 90% of mechanical properties but also retains

excellent optical properties (\({T}_{550{\rm{nm}}}\) ~ 88%) and thermal stability (\({T}_{5 \% }\) ~ 506 °C). The design strategy paves the way for enhancing the durability of PIs for energy

conversion and electronic applications resisting harsh conditions. SIMILAR CONTENT BEING VIEWED BY OTHERS MECHANICAL-ROBUST AND RECYCLABLE POLYIMIDE SUBSTRATES COORDINATED WITH CYCLIC

TI-OXO CLUSTER FOR FLEXIBLE ORGANIC SOLAR CELLS Article Open access 06 June 2022 IMPROVED PHOTOVOLTAIC PERFORMANCE AND ROBUSTNESS OF ALL-POLYMER SOLAR CELLS ENABLED BY A POLYFULLERENE GUEST

ACCEPTOR Article Open access 22 April 2023 ULTRA-FLEXIBLE SEMITRANSPARENT ORGANIC PHOTOVOLTAICS Article Open access 03 June 2023 INTRODUCTION Aromatic polyimides (PIs) are well known for

their superior flexibility as well as high thermal and mechanical properties originating from their rigid molecular structures and inter/intramolecular interactions1,2. Recently, the rapid

advancement of optoelectrical applications such as flexible organic solar cells as well as flexible smart windows entails the development of colorless and optical transparent PIs3,4,5,6.

These colorless polyimides (CPIs) also must maintain their physical and optical integrity under harsh operating conditions, especially high-intensity UV irradiation. As for the transparency

consideration7, structural design approaches such as introducing asymmetric structure8, fluorine-containing group6, aliphatic9, and ether bonds10 as well as electron-withdrawing groups have

been proven to be efficient by minimizing or eliminating the formation of charge transfer complexes (CTCs). However, effective approaches to the simultaneous environmental stability,

especially UV resistance, of transparent CPIs are still lacking. It has been found that UV irradiation can severely deteriorate PIs11,12,13,14,15,16, which leads to the cleavage of chemical

bonds, defects such as cracks, voids, and mass loss, and finally caused degradation of comprehensive properties and significantly reduced their lifetime. For example, Tanaka et al.16 found

that UV irradiation in air could cause oxidative cleavage of the imide ring followed by bridging between the polymer chains. In addition, Taniike et al.14 investigated the photodegradation

of the bio-derived polyimide and found that elongated radiation caused deterioration at the imide ring and the tertiary carbon of the cyclobutene ring with the growth of carbonyl species.

Our previous work has shown that after UV irradiation, CPIs experienced significant deterioration of mechanical properties and thermal stability, as well as the breakage of the ether bond,

imide ring, and phenyl groups11,12. Recently, different methods for the enhancement of UV resistance of PIs were explored, including the incorporation of a light stabilizer/UV absorber in

the bulk matrix17,18,19,20 or protective coating on the surfaces21,22. Nevertheless, the migration of stabilizers from the matrix due to their low solubility or the delamination of coated

materials can lead to significant deterioration of their UV protection ability. Alternatively, bulk structural design can be another promising strategy for the intrinsic enhancement of the

UV resistance ability of CPIs. One of the most challenging issues is how to balance the optical transparency, UV resistance, and thermal stability to achieve excellent comprehensive

properties. This is mainly because those goals contradict each other from the perspective of structural design, owing to the lack of a deep understanding of the quantitative

structure-property relationship. Herein, a facile strategy was utilized to synthesize a series of CPI films by introducing trifluoromethyl, fluorene, or ether groups. It is expected that

those groups affect the electronic states in CPIs and the intra/inter charge transfer interactions, which determined the comprehensive properties of CPIs. The optical, thermal, mechanical,

and especially UV resistance behaviors of the CPIs containing different structures were carefully studied and the underlying mechanisms were explored. It was found that with subtle

manipulation of charge transfer interaction and the conjugation effects of CPIs, a balance between different key performances can be achieved. This work aims to provide deep insights and

practical hints into the structural design strategies for high-performance CPIs toward optoelectrical applications under harsh conditions. RESULTS AND DISCUSSION SYNTHESIS AND

CHARACTERIZATIONS OF CPI FILMS 4 types of colorless polyimides (CPIs) films containing trifluoromethyl, fluorene, or ether groups, which were designated as CPI-1 to CPI-4 (6FDA-BAPF,

6FDA-TFMB, BPADA-BAPF, and BPADA-TFMB), were synthesized and characterized systematically. Different combinations of trifluoromethyl, fluorene, or ether groups were designed, aiming to

control the charge transfer interactions between electron-donating diamine and electron-accepting dianhydride moieties. Figure 1a, b gave their molecular structures as measured by FTIR and

NMR. As shown in Fig. 1a, the peak near 1175 cm−1 corresponded to the deformation of the C-N-C in the imide ring, while peaks around 1367 cm−1 corresponded to the axial stretching of the C-N

bond12. Peaks near 1475 and 1625 cm−1 were attributed to the stretching vibration of the C=C bond in the benzene ring, and the peaks near 1781 and 1720 cm−1 corresponded to the stretching

vibration of the C=O bond23. Those results clearly demonstrated the formation of imide ring structures. Specifically, for CPI-1, the stretching vibration of the C-F bond was observed at 1140

 cm−1 24, indicating the introduction of trifluoromethyl structures. For CPI-2, a significant peak of the C-F bond stretching vibration was observed near 1122 cm−1 due to the introduction of

hexafluorodiamine and hexafluorodianhydride structures. Peaks at 1076 and 1236 cm−1 were observed in CPI-3 and CPI-4, which can be ascribed to the stretching vibration of the C-O-C bond10,

indicating the presence of ether bonds in the aromatic ring structure. The successful introduction of trifluoromethyl structure can be proved by the appearance of the C-F bond stretching

vibration peak at 1124 cm−1 in CPI-4. Besides, Fig. 1b showed that peaks near 1.79 ppm corresponded to -CH3 of the BPADA25. Peaks at 2.7 ppm and 2.9 ppm corresponded to DMF. Peaks around

7.2–7.5 ppm were ascribed to H of the fluorene26, and peaks of TFMB were around 7.62–7.64 ppm27. Moreover, peaks around 8–8.1 ppm corresponded to H in the 6FDA benzene ring27. In addition,

Fig. 1c exhibited the molecular weight distribution curves of CPI films. _M_w of CPI films ranged from 120000 to 160000, which was in the typical range of CPIs. Moreover, all CPI films were

basically amorphous (Fig. 1d), as the arrangement of the molecular chains was disrupted by the dense aromatic structure and large asymmetric groups1,2. These results together confirmed the

designed chemical structures of CPIs. To get a deep understanding of the conjugation effects of different CPI films, density functional theory simulation was used to theoretically calculate

molecular orbital energies of different structures, as shown in Fig. 2. The balls with gray, white, red, blue, and light blue represented C, H, O, N, and F atoms, respectively. In addition,

in the highest occupied molecular orbital (HOMO) and the lowest unoccupied molecular orbital (LUMO), the red part of the molecular structure represented the positive phase part, and the

green part represented the negative phase part. \({E}_{{LUMO}}\) was used to measure the electron-accepting ability of dianhydride; the larger the value of \({E}_{{LUMO}}\), the stronger

ability of accepting electrons of dianhydride. \({E}_{{HOMO}}\) was used to represent the electron-donating ability of diamine and larger \({E}_{{HOMO}}\) reflected stronger

electron-donating ability of diamine. The \({E}_{{LUMO}}\) values of CPI-1, CPI-2, CPI-3, CPI-4, and traditional yellow PI film were calculated to be −2.87 eV, −3.08 eV, −2.38 eV, −2.53 eV,

and −3.43 eV, respectively. The \({E}_{{HOMO}}\) values of CPI-1, CPI-2, CPI-3, CPI-4, and traditional yellow PI film were −6.07 eV, −7.11 eV, −5.95 eV, −6.76 eV, and −6.29 eV, respectively.

Energy band gap (\(\Delta {E}_{{\rm{gap}}}\)) was further calculated to evaluate the charge transfer interactions, which was related to the color of CPI films directly. It was accepted that

the order of calculated band gaps was approximately parallel to that of absorption edge wavelengths of the experimental spectra28. \(\Delta {E}_{{\rm{gap}}}\) of CPI-1, CPI-2, CPI-3, CPI-4,

and traditional yellow PI film were 3.20 eV, 4.03 eV, 3.57 eV, 4.23 eV, and 2.86 eV respectively. The results showed that the \(\Delta {E}_{{\rm{gap}}}\) of all CPI films was significantly

higher than that of traditional yellow PI film, and they were quite different. Note that DFT calculation only can quantitatively picture the light absorption of PIs, while more quantitative

theoretical predictions needed additional correction by considering effects from the condensed phase28. Overall, the charge transfer interactions can be tuned in a wide range by the

introduction of trifluoromethyl, ether bond, or fluorene groups, which made it feasible to balance different properties to achieve excellent comprehensive performance. INITIAL PERFORMANCE OF

CPI FILMS Figure 3a showed the UV-Vis transmittance spectra and yellowness index (YI) of CPI films. All CPI films exhibited outstanding transmittance (\({T}_{550{\rm{nm}}}\) >88%) and

relatively low YI (<5.9). This result arose from the well-chosen diamines and dianhydrides, which changed the electron cloud distribution and reduced CTCs within their molecular

chains29,30. The YI of CPI films followed the order: CPI-1 > CPI-3 > CPI-4 ≈ CPI-2. Further comparison of the overall optical properties of CPI films with that reported in the

literature was carried out by employing Ashby plots (Fig. 3b). \({T}_{550{\rm{nm}}}\) and YI were represented in \(x\) and \(y\)-axes, respectively. Data points located in the right corner

represented the best comprehensive optical properties. CPI films synthesized in this work possessed excellent overall optical performance, which was comparable to that in the

literature31,32,33,34,35 and superior to that of representative traditional yellow PI films36,37. Crucial mechanical and thermal performances that determined the applicability of CPI films

in photoelectric fields were further compared, as shown in Fig. 4. The tensile strength of CPI films were 111.3 MPa, 94.4 MPa, 94.6 MPa, and 99.9 MPa, respectively, and Young’s modulus were

2.7 GPa, 3.5 GPa, 2.3 GPa, and 2.4 GPa respectively, as shown in Fig. 4a. The high molecular weight of the synthesized films and aromaticity density might account for their excellent

mechanical properties. Compared with CPI-3 and CPI-4, the higher Young’s modulus of CPI-1 and CPI-2 could be mainly attributed to their more rigid skeletal structures10,38. The elongation at

break of CPI films were 8.7, 4.7, 11.9, and 48.7%, respectively. Compared with CPI-3 and CPI-4, CPI-1 and CPI-2 exhibited lower elongation at break due to their high aromaticity density,

resulting in brittle behavior. In contrast, ether bonds introduced into CPI-3 and CPI-4 contributed to enhancing the flexibility of molecular chains, resulting in a higher elongation at

break10. Overall, CPI-3 and CPI-4 exhibited decent comprehensive mechanical properties with a balance of strength-ductility as a result of synergistic effects of ether bond, fluorene, or

trifluoromethyl structure39. The thermal degradation mechanism of polyimide mainly involved the cleavage of molecular chains, producing volatile products such as carbon monoxide, carbon

dioxide, and carbonized benzene rings and leading to weight loss (Fig. 4b). Furthermore, two distinct weight loss stages were observed in derivative thermogravimetric curves for CPI-1 and

CPI-2 (Fig. 4c). The first stage, occurring around 550 °C, was mainly attributed to the thermal cleavage of C-N bonds or C-C bonds, resulting in the opening of imide rings. Then, active free

radicals and small molecule gases such as CO and CO2 could be generated under higher temperature conditions40. The second stage, occurring at temperatures greater than 620 °C, exhibited a

gradually slowing weight loss rate due to the carbonization process of pyrolytic dehydrogenation of the benzene ring40,41,42. However, for CPI-3 and CPI-4, obvious weight loss occurred at a

much lower decomposition temperature around 530 °C, presumably due to the decomposition of C-O-C, which has much worse decomposition stability and was easier to break43. It was found that

the onset decomposition temperature (\({T}_{5 \% }\)) and temperatures of the maximal rate of weight loss (\({T}_{\max }\)) of CPI-3 and CPI-4 were lower than that of CPI-1 and CPI-2 (Fig.

4d, e). In addition, all CPI films possessed a relatively high \({T}_{{\rm{g}}}\) (Fig. 4f), with values of 412, 359, 312, and 255 °C for CPI-1 ~ CPI-4 respectively. The relatively higher

\({T}_{{\rm{g}}}\) of CPI-1 and CPI-2 can be attributed to the increase in the spatial barrier and the increase in molecular chain rigidity30,44,45, while the introduction of ether bond

lowered \({T}_{{\rm{g}}}\) of CPI-3 and CPI-4 due to the increase in the flexibility of the material and the reduction of the energy barrier for chain movement. UV RESISTANCE OF CPI FILMS

The harsh working environments of optoelectrical applications, especially under high UV irradiation, presented a great challenge for CPI films. To this end, we further investigated the UV

stability of CPI films with different structures by monitoring the effects of UV irradiation on their key properties. Effects of UV irradiation on the optical properties were monitored by

UV-Vis spectra and YI, as shown in Fig. 5. An obvious enhancement of the absorption around 400 nm was observed for CPI-1, CPI-2, and CPI-4, accompanied by significant yellowing.

Specifically, upon UV irradiation, YI of CPI-1, CPI-2, and CPI-4 significantly increased to 16.11, 17.2, and 13.46 respectively. In contrast, CPI-3 exhibited the most obvious resistance to

yellowing, with YI of only 9.63 after being aged. The optical transparency of CPI-3 is also almost unchanged (\({T}_{550{\rm{nm}}}\) ~88%). Figure 6 gave the changes in mechanical and

thermal properties of CPI films. After UV irradiation for 168 h, the tensile strength of CPI-1 ~ CPI-4 were decreased by about 77.5, 87.3, 4.4, and 36.0%, respectively (Fig. 6a). Among them,

CPI-3 showed the best mechanical integrity, which possessed the highest tensile strength of about 90 MPa after UV irradiation. A similar trend was observed for Young’s modulus and

elongation at break (Fig. 6b, c). Fair high retentions of 89 and 88% for Young’s modulus and elongation break of CPI-3 were observed respectively after UV irradiation. The excellent UV

stability of CPI-3 could be due to its peculiar conjugation structures resulting from the introduction of the fluorene unit into the molecular chain. Figure 6d showed that weight loss

happened for all CPI films during UV aging, probably due to the loss of fragments on the surface and the volatilization of gaseous degradation species such as CO and CO246. CPI-3 exhibited

the least loss of weight with a residual weight of 97.1% after UV irradiation for 168 h, while the residual weight of 90.6, 95.5, and 93.5% after UV irradiation were observed for CPI-1,

CPI-2, and CPI-4 respectively. Figure 6e illustrated the thermogravimetric curves of CPI films. After UV irradiation, an obvious reduction of the thermal stability of CPI-1 and CPI-2 was

observed. Specifically, \({T}_{5 \% }\) was decreased by 19.4 and 12.7% for CPI-1 and CPI-2 (Fig. 6f), respectively. In contrast, a minor increase of about 0.6 and 0.5% for \({T}_{5 \% }\)

of CPI-3 and CPI-4 was observed. Overall, CPI-3 exhibited superior mechanical and thermal performance after UV irradiation. The changes in the optical, mechanical, and thermal performance of

CPI films were mainly related to the changes in the molecular structure caused by UV irradiation. We further conducted the solubility, GPC and FTIR tests for different CPI films to

understand the molecular structure changes during UV irradiation. We first conducted solubility tests for CPI films in different types of common organic solvents including Dimethylacetamide

(DMAc), Dimethylformamide (DMF), and Tetrahydrofuran (THF), and the results were shown in Table 1. The solubility of CPIs was roughly classified as −, +−, and ++, which represent insoluble,

partially soluble or soluble respectively at room temperature. For the fresh samples, CPI-1 and CPI-2 only can be partially soluble in different common solvents, while CPI-3 and CPI-4 were

more soluble. After UV aging, all the samples showed good solubility in different solvents without any insoluble parts. These results implied that UV irradiation shall enhance the solubility

of CPI films mainly by chain scission. In addition, the molecular weight distribution curves and retention percentage of _M_w were shown in Fig. 7. Molecular weight distribution curves

shifted to the low molecular weight part after 168 ‍h of UV irradiation (Fig. 7a), indicating a significant decrease in molecular weight due to the breaking of the chain structure. These

results were consistent with that of solubility tests. Moreover, the retention percentage of _M_w of CPI-3 aged for 168 h was the highest with a value of 59%, confirming the relatively

stable nature of CPI-3 (Fig. 7b). Figure 8 gives the UV-induced evolutions in the molecular structure of different CPI films as monitored by FTIR spectra. The Pearson normalization method

was used to process those spectra, following a similar procedure reported in the literature14,47. After UV irradiation, decay of peak intensity around 1360 cm−1 assigned to the C-N bond in

the imide ring was observed for all CPI films (Fig. 8a–d), without the emergence of any new characteristic peaks. The main structural change of CPI films induced by UV irradiation could be

the ring opening and breakage of C-N12. Specifically, after UV aging for 168 h, the C-N index (Fig. 8e) underwent a decrease by 37, 26, 13, and 33% for CPI-1, CPI-2, CPI-3, and CPI-4,

respectively. CPI-3, which contained fluorene groups and C-O-C bonds, experienced the least chain breakage and the best UV resistance. In addition, the evolution of C=O bonds was also

monitored (Fig. 8f). It shall be noted that different from C-N bonds, both the formation and depletion of C=O bonds could happen during the oxidation and degradation of CPI film11,14. After

UV aging, reduction in the content of C=O bonds were actually observed for all CPI films, which indicating that the depletion of C=O bonds could be dominated. Taken together, the FTIR

results showed that chain scission mainly happened for all CPI films during UV irradiation, which supplemented the observations from solubility and GPC tests. The typical degradation

mechanism of CPI films for the deterioration of mechanical and optical properties can be deduced and summarized in Fig. 8g. Under ultraviolet irradiation, ring opening shall happen and the

C-N bond in polyimide can be broken and combined with oxygen, giving free radicals and volatile products such as alkane gas, CO2, etc. Those chain scission mechanisms shall be responsible

for the deterioration of the thermal or mechanical properties of CPI films48,49. We further built a pentagonal radar chart to visually compare the key structure and performance of CPI films

after UV aging, as shown in Fig. 9. Upon UV irradiation, the retention of the C-N bond of CPI-3 films was higher than that of other CPI films, indicating its least chain scission. Moreover,

the tensile strength and elongation at break of CPI films were the highest after UV irradiation. In contrast, CPI-1 and CPI-2 underwent a severe degradation in the mechanical properties

during UV aging, due to the breakage of the C-N and C=O bond as well as the opening of the imide ring46. In addition, poor thermal stability and significant discoloration were also observed

in CPI-1, CPI-2, and CPI-4 films after UV irradiation, while CPI-3 maintained its high thermal stability and low discoloration with \({T}_{5 \% }\) of 506 °C and YI of 9.63. Overall, the

introduction of fluorene and the strong conjugation effect made the molecular chains of CPI-3 interact with each other more strongly, leading to its excellent UV resistance. To further

reveal the UV resistance mechanisms of CPI-3, the potential UV energy dissipation paths for CPI-3 were explored. In general, the polymer molecular chain was excited after absorbing UV energy

and jumps from the stable ground state (\({S}_{0}\)) to the high-energy excited state (\({S}_{1}\)), as shown in Fig. 10a. The atoms in the excited state were generally

unstable45,50,51,52,53; as a result, the UV stability of the material was mainly determined by whether the excited molecules can return to their original state by efficiently harmlessly

dissipating the absorbed energy. In this regard, energy dissipation in the form of fluorescence or thermal radiation was preferred, both of which have been found to work for CPI-3. The first

dissipation path, which is the release of energy through fluorescence radiation, was shown in Fig. 10b. Under near-UV wavelength excitation at 405 nm, only relatively low fluorescence

emission was observed for CPI-1 (maximum fluorescence intensity of 32.3), CPI-2 (29.3), and CPI-4 (90.5), which could be due to the presence of trifluoromethyl54. However, CPI-3, which

contained fluorene, isopropylidene, and ether groups, showed a very strong fluorescence emission (157.2), probably due to the increased density of aromatic rings in the molecular chain and

contributed to the conjugation in the polyimide molecular structure, enhancing the π-π* leap of the molecule55,56. It has been reported that the existence of an isopropylidene group or ether

group could enhance the fluorescence emission ability of CPIs. For example, Wu et al.57 found that PIs containing the isopropylidene group exhibited higher fluorescence intensity

(approximately 5000 a.u.) compared to OH-6FDA containing the trifluoromethyl group (approximately 1000 a.u.). In addition, the interchain interactions could also contribute to the higher

fluorescence emission of CPI-328. The path of the thermal radiation mechanism was further verified by infrared thermography. The thermal images of CPI films were taken under UV radiation at

a wavelength of 365 nm, as shown in Fig. 10c. The maximum temperatures of CPI-1 to CPI-4 were 34.3, 32.8, 42.1, and 38 °C, respectively. The heat release could be due to the vibration,

rotation, and motion of atoms and molecules induced by higher energy58, or the out-of-plane deformation of ring centers, mutual isomerization50, etc. CPI-3 exhibited the highest radiation

temperature, which demonstrated that thermal radiation was another effective way for the dissipation of UV energy. Furthermore, the UV resistance of CPI-3 was also compared with that of

traditional yellow PI film, which mainly consisted of pyromelliticacidanhydride (PMDA) and 4,4’-Oxydianiline (ODA). The evolution in tensile strength and onset decomposition temperature of

the traditional yellow PI film (PMDA-ODA) and CPI-3 (BPADA-BAPF) during UV aging were studied for up to 336 h (Fig. 11). The tensile strength of both CPI-3 and traditional yellow PI were

decreased gradually over aging time. For example, the tensile strength of fresh traditional yellow PI was decreased from 132.2 ± 3.3 MPa to 108.6 ± 10.5 MPa by 18% after 336 h, while was

decreased from 94.6 ± 12.5 MPa to 45.1 ± 3.0 MPa by 52% for CPI-3. In addition, after 336 h of UV aging, only a minor reduction in \({T}_{5 \% }\) was observed for both traditional yellow PI

and CPI-3. Taken together, these results indicated that CPI-3 showed decent UV resistance at an extended aging time, even though it was slightly inferior to that of traditional yellow PI

film. In this work, a series of CPI films with different charge transfer interactions were synthesized by introducing trifluoromethylene, fluorene, or ether bonds. The relationship between

their structures and UV resistance as well as optical properties and mechanical properties etc. were explored. It was found that the simultaneous introduction of trifluoromethylene and

fluorene significantly improved the optical transparency, thermal stability, and mechanical strength of CPI films. Moreover, the introduction of trifluoromethylene and flexible ether bonds

effectively improved the optical transparency and toughness. Note that the existence of isopropylidene, ethers and fluorenes effectively endowed CPI film (CPI-3) with optimal UV resistance

and decent initial performance (optical transparency, thermal stability, and toughness) simultaneously. Specifically, after being subjected to high-intensity UV irradiation, CPI-3 not only

maintained over 90% of its mechanical properties but also retained its high optical properties (\({T}_{550{\rm{nm}}}\) ~ 88%) and thermal stability (\({T}_{5 \% }\) ~ 506 °C). The UV

stability of CPI-3 was attributed to its efficient dissipation ability of absorbed UV energy via the routes of both fluorescence emission and photothermal conversion. The optimized

comprehensive performance of CPI-3 could be related to its sophisticated charge transfer interaction in the conjugation structure. The design strategy paved the way for optimizing the

durability of polyimides for energy conversion and electronic applications resisting harsh conditions. METHODS MATERIALS 4,4’-(Hexafluoroisopropylidene)diphthalic Anhydride (6FDA),

4,4’-(4,4’-Isopropylidenediphenoxy)diphthalic Anhydride (BPADA), 9,9-Bis(4-aminophenyl)fluorene (BAPF), and 2,2’-Bis(trifluoromethyl)benzidine (TFMB) were purchased from Shanghai Macklin

Biochemical Technology Co., Ltd. Anhydrous N-N-Dimethylacetamide (DMAc) were purchased from Shanghai Aladdin Biochemical Technology Co., Ltd., while anhydrous ethanol, acetic anhydride, and

pyridine were purchased from Chengdu Cologne Chemical Co., Ltd. All monomers were carefully dried before any use. SYNTHESIS AND FABRICATION OF POLYIMIDE (PIS) FILMS A series of aromatic

polyimides (CPIs) were synthesized by introducing trifluoromethyl, fluorene, or ether groups, including 6FDA-BAPF (CPI-1), 6FDA-TFMB (CPI-2), BPADA-BAPF (CPI-3), and BPADA-TFMB (CPI-4), as

shown in Fig. 12a. A general procedure for the fabrication of CPIs was illustrated by the synthesis of CPI-3 (Fig. 13). First, BAPF (1.74 g, 5 mmol) and anhydrous DMAc (17.5 ml, 20 wt%) were

added into a 50 mL flask, stirring for 20 min under a nitrogen atmosphere to completely dissolve. 6FDA (2.628 g, 5.05 mmol) was then added into the above mixture solution in three batches.

The mixture solution was stirred at room temperature for 8 h to obtain a transparent polyamic acid (PAA). In the process of chemical imidization, pyridine needed to be added as a catalyst

and acetic anhydride as a dehydrating agent, and finally, a polyimide glue solution was obtained. The PAA solution was coated on a 10 cm × 10 cm glass plate by an experimental coater

(MS-ZN320B, Xiamen, China), and then placed in an oven for high-temperature imidization. The PAA solution was dried at 30, 80, and 120 °C for 2 h, respectively, to remove most of the solvent

slowly without the formation of bubbles, and to start a pre-imidization process. Then it was imidized at 180, 220, 270, and 300 °C for 1 h, respectively to complete the imidization process.

Finally, the colorless polyimide (CPI) films with a thickness of around 30 μm were successfully synthesized by adjusting the appropriate solid content. For comparison, traditional yellow PI

film consisted of pyromelliticacidanhydride (PMDA) and 4,4’-Oxydianiline (ODA) were also synthesized following a similar procedure (Fig. 12b). UV AGING TEST CPI films were cut into 5 cm × 5

 cm squares and loaded in a homemade photo-oxidation aging apparatus with an iodine-gallium lamp (500 W) and a temperature-control system (Fig. 14). The direct distance between the film and

the iodine-gallium lamp was controlled to be 30 cm. The exposure intensity was 10 ± 3 W m−2 measured by a UV-A luminometer (Beijing Normal University Photoelectric Instrument Factory) and

the temperature was constant at 30 ± 1 °C. The maximum intensity of the UV exposure was 365 nm. Samples were collected regularly for the characterization of structure and properties.

CHARACTERIZATIONS CHEMICAL STRUCTURES FTIR spectra were obtained by testing polyimide films on a Nicolet 6700 (Thermo Fisher Scientific) spectrometer in attenuated total reflectance mode

with a resolution of 4 cm−1 and 32 scans in the region between 650 and 4000 cm−1. Infrared spectra were normalized by spectral area from 650 to 2000 cm−1 to analyze the changes in group

content during aging14,47. The C-N and C=O functional group indices were calculated by intensity of the normalized C-N and C=O bond peak, respectively. 1H-NMR and 13C-NMR spectra were

conducted on a Bruker 400 M apparatus, in which all CPI films were dissolved in N, N-Dimethylformamide-d7 (DMF-d7). The crystalline properties of CPI films were measured by a Smart Lab XRD

(Rigaku Co., Japan). The copper target was selected for testing, with a scanning range of 5~90° and a scanning speed of 2° min−1. The average molecular mass was measured by an HLC8320 GPC

(Tosoh Co., Tokyo, Japan). DMF was used as the mobile phase, the test temperature was room temperature, polystyrene was selected as the standard sample, the injected sample volume was 10 μL,

and the running time was 15 min. The solubility test was characterized by cutting various CPI films into 10 mg at room temperature (25 °C) and dissolving them in different aprotic solvents

for 24 h. CALCULATION OF QUANTUM CHEMISTRY To understand the conjugation effects in molecules, the energy levels of the molecular orbits of CPI films were calculated by density functional

theory (DFT) / B3LYP/6-311G(d, p) with the Gaussian 16 program package59. Gaussian 16 was used to optimize and analyze the frequency of four initial structures. B3LYP was used as the

function and 6–31 g(d) was used as the basis set. Subsequently, the molecular orbital analysis of molecular structure was carried out by GaussView 6.0. OPTICAL PROPERTIES The transmittance

of the CPI films was measured in the wavelength range of 200–800 nm by using the Lambda 750 S UV-VIS-NIR spectrum of PerkinElmer. In addition, the CIE index and yellowness index (YI) were

measured using a spectrophotometer (TS7020, 3nh®), following ASTM E 313-20. Measurements were taken using a D65 standard illuminant and a 10-degree observer in a planar viewing mode. For

optical testing, CPI films with a size of 10 × 10 cm were used, and five points were selected for testing. ASTM E 313-20: $${\rm{YI}}=100(1.3013X-1.1498Z)/Y$$ (1) where _X_, _Y_, and _Z_

were the measured tristimulus values. THERMAL AND MECHANICAL PROPERTIES To probe the thermal behaviors of CPI films, thermogravimetric analysis (TGA) was performed under a nitrogen

atmosphere by using TGA 550 (TA Instrument, USA). The temperature was increased from 25 to 800 °C at a heating rate of 10 °C min−1. Before tests, CPI films were dried in an oven to avoid the

effect of moisture on tests. Dynamic thermomechanical analysis (DMA) was carried out on a Q850 (TA Instruments, USA) in the tensile mode. The temperature ranged from −30 to 400 °C, with a

heating rate of 5 °C min−1, a frequency of 1 Hz, and an amplitude of 10 μm. For CPI-1 to CPI-4, samples with dimensions of 6 × 6 mm × 30 μm were used. Mechanical properties of CPI films were

obtained on a universal mechanical testing machine (INSTRON 5967, USA) with a speed of 5 mm s−1 and a gauge length of 15 mm. CPI films with the dimensions of 6 × 35 mm rectangles were used.

At least five replicated samples were measured. Fluorescence imaging was performed using a Leica SP8 laser scanning confocal microscope (Leica Microscopy, Wetzlar, Germany) with a near-UV

excitation wavelength of 405 nm. IR thermographic images of the CPI films were taken using a FLUKE Ti32S thermal imager (Fluke Infrared Camera, Shanghai, China) at a wavelength of 365 nm

with an 80 W high-power UV LED light. DATA AVAILABILITY All data generated or analyzed during this study are included in this published article and any additional data that support the

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National Natural Science Foundation of China (U19A2096, 52003175), Department of Science and Technology of Sichuan Province under grant number of 2022NSFSC2012, the Fundamental Research

Funds for the Central Universities. AUTHOR INFORMATION AUTHORS AND AFFILIATIONS * College of Polymer Science and Engineering, State Key Laboratory of Polymer Materials Engineering of China,

Sichuan University, Chengdu, 610065, China Le Xi, Yadong Lv, Jiabao Feng, Yajiang Huang, Qi Yang & Guangxian Li * School of Mechanical Engineering, Chengdu University, Chengdu, 610000,

China Yanyan Huang * School of Aeronautics and Astronautics, State Key Laboratory of Polymer Materials Engineering of China, Sichuan University, Chengdu, 610065, China Miqiu Kong Authors *

Le Xi View author publications You can also search for this author inPubMed Google Scholar * Yadong Lv View author publications You can also search for this author inPubMed Google Scholar *

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inPubMed Google Scholar CONTRIBUTIONS L.X.: Investigation, writing original draft & editing. Y.L.: Conceptualization, Project administration, Writing - review & editing. J.F.:

Writing - review & editing. Yanyan.H.: Writing - review & editing. Yajiang.H.: Writing - review & editing. Q.Y.: Writing - review & editing. G.L.: Writing - review &

editing. M.K.: Conceptualization, Funding acquisition, Writing - review & editing. CORRESPONDING AUTHORS Correspondence to Yadong Lv or Miqiu Kong. ETHICS DECLARATIONS COMPETING

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THIS ARTICLE CITE THIS ARTICLE Xi, L., Lv, Y., Feng, J. _et al._ Synthesis of UV-resistant and colorless polyimide films for optoelectrical applications. _npj Mater Degrad_ 8, 6 (2024).

https://doi.org/10.1038/s41529-023-00422-w Download citation * Received: 10 August 2023 * Accepted: 26 December 2023 * Published: 11 January 2024 * DOI:

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