Date Palm Tree Leaf-Derived Cellulose Nanocrystal Incorporated Thin-Film Composite forward Osmosis Membranes for Produced Water Treatment

Worldwide water shortage and significant issues related to treatment of wastewater streams, mainly the water obtained during the recovery of oil and gas operations called produced water (PW), has enabled forward osmosis (FO) to progress and become advanced enough to effectively treat as well as retrieve water in order to be productively reused. Because of their exceptional permeability qualities, thin-film composite (TFC) membranes have gained increasing interest for use in FO separation processes. This research focused on developing a high water flux and less oil flux TFC membrane by incorporating sustainably developed cellulose nanocrystal (CNC) onto the polyamide (PA) layer of the TFC membrane. CNCs are prepared from date palm leaves and different characterization studies verified the definite formations of CNCs and the effective integration of CNCs in the PA layer. From the FO experiments, it was confirmed that that the membrane with 0.05 wt% of CNCs in the TFC membrane (TFN-5) showed better FO performance in PW treatment. Pristine TFC and TFN-5 membrane exhibited 96.2% and 99.0% of salt rejection and 90.5% and 97.45% of oil rejection. Further, TFC and TFN-5 demonstrated 0.46 and 1.61 LMHB pure water permeability and 0.41 and 1.42 LHM salt permeability, respectively. Thus, the developed membrane can help in overcoming the current challenges associated with TFC FO membranes for PW treatment processes.


Introduction
One of the most substantial forms of wastewater production related to oil and gas is produced water (PW), and it is a water-in-oil emulsion in which the surface-active agentstabilized oil phase is properly disseminated in the aqueous phase [1]. Different materials have been developed for solving the challenging marine oil spill pollution problem [2,3]. Currently, PW is the leading wastewater type in the oil and gas sector, including an estimated worldwide volume-to-product ratio of 3:1. PW contains organic and inorganic matters, dispersed oils, suspended particles, greases, hydrocarbons, and dissolved solutes, which makes it one of the most complicated liquid wastes. The typical composition of PW includes 15 to 300 mg/L of oil and grease, 1000 to 15,000 mg/L of total dissolved solids (TDS), 20 to 2500 mg/L of chemical oxygen demand (COD), and 5 to 4000 mg/L of total suspended solids (TSS) [4]. As there is a significantly high amount of these components in PW, it can negatively impact human health and the natural environment; it is very important to properly treat the PW. Furthermore, more technical advancements are needed to comply with the stricter regulatory standards for PW discharge [5,6]. The traditional PW treatment techniques do not generally meet the discharge limits of PW, as low hydrocarbon content in the PW is not effectively separated and also specifically fails to remove oil droplets in PW that are finely scattered [7,8]. Furthermore, this traditional treatment is expensive, requires chemical use, generation of secondary waste, and only works until FO requires a lower energy consumption, which is a significant advantage in order to reduce the amount of PW as an oil/brine waste [38][39][40]. Out of the different techniques examined for PW treatment, FO was recognized as a technology that can withstand certain PW processes having increased TDS [41]. In spite of the numerous advantageous of using a TFC FO membrane for PW treatment application, it is very important to solve the related challenges such as a low water flux, a high oil flux, and the fouling tendency of the TFC membrane. Contemplating the different PW constituents, the propensity of membrane fouling will be greater compared to any other wastewater. In comparison to its CTA counterparts, the TFC membranes are more prone to fouling, especially when used with challenging feed solutions like oil/water mixtures [42,43]. This can be due to high surface roughness, strong hydrogen bonding capability, and a high initial water flux [44]. The aforementioned challenges of FO TFC membranes may be mitigated by integrating appropriate nanomaterials into the selective layer of the TFC membrane. The selective layer of the TFC membrane is the most important parameter that governs overall membrane performance [45,46]. In addition, the high rejection ability of the selective layer assures strong oil rejection, which results in high water recovery [31,34].
Cellulose nanocrystals (CNC) or nanocrystalline cellulose (NCC) are the derivatives of cellulose that are prepared through acid hydrolysis of cellulose, in which the cellulose is added to sulfuric acid under a controlled temperature as well as time period [47]. Recently, biodegradable CNC has received considerable research interest in several applications. Cellulose consisting of crystalline and amorphous areas is the critical foundation of plant fibers [48]. This can provide mechanical integrity, and therefore can be utilized to reinforce membrane materials, polymers, and bio nanocomposites [49]. CNC has a rod- FO requires a lower energy consumption, which is a significant advantage in order to reduce the amount of PW as an oil/brine waste [38][39][40]. Out of the different techniques examined for PW treatment, FO was recognized as a technology that can withstand certain PW processes having increased TDS [41]. In spite of the numerous advantageous of using a TFC FO membrane for PW treatment application, it is very important to solve the related challenges such as a low water flux, a high oil flux, and the fouling tendency of the TFC membrane. Contemplating the different PW constituents, the propensity of membrane fouling will be greater compared to any other wastewater. In comparison to its CTA counterparts, the TFC membranes are more prone to fouling, especially when used with challenging feed solutions like oil/water mixtures [42,43]. This can be due to high surface roughness, strong hydrogen bonding capability, and a high initial water flux [44]. The aforementioned challenges of FO TFC membranes may be mitigated by integrating appropriate nanomaterials into the selective layer of the TFC membrane. The selective layer of the TFC membrane is the most important parameter that governs overall membrane performance [45,46]. In addition, the high rejection ability of the selective layer assures strong oil rejection, which results in high water recovery [31,34].
Cellulose nanocrystals (CNC) or nanocrystalline cellulose (NCC) are the derivatives of cellulose that are prepared through acid hydrolysis of cellulose, in which the cellulose is added to sulfuric acid under a controlled temperature as well as time period [47]. Recently, biodegradable CNC has received considerable research interest in several applications. Cellulose consisting of crystalline and amorphous areas is the critical foundation of plant fibers [48]. This can provide mechanical integrity, and therefore can be utilized to reinforce membrane materials, polymers, and bio nanocomposites [49]. CNC has a rod-like nanostructured material isolated by cellulose through the means of acid hydrolysis. CNC shows superior characteristics, such as biodegradability, biocompatibility, non-toxic nature, cost effectiveness, good mechanical properties, and high hydrophilicity [50]. These remarkable characteristics indicate the enormous possibility of CNC when integrated in water treatment membranes [51]. CNCs are currently employed in several applications, such as in water purification as adsorbents, flocculants, membranes, and absorbents [52,53]. Cellulose was incorporated in mixed matrix membranes for microfiltration and ultrafiltration; additionally, it was added in the thin-film nanocomposite (TFN) membranes in RO and FO membranes. Certain preparation techniques could increase the nanocellulose's surface area to 500 m 2 /g. The intrinsic hydrophilic property of CNC is anticipated to increase flux and decrease the fouling propensity of the membrane. According to Rezaei-Dasht Arzhandi et al. [54], the fouling resistance and water flux of the TFC FO membrane was enhanced by the incorporation of nanocrystalline cellulose into the selective layer of the membrane. Azar et al. [32] modified PES, which was designated as the support of the TFC membrane using two different nanomaterials (CNC and NC with serine amino acid), and tested the FO performance of the membrane. It was noticed that due to the addition of CNC, the hydrophilicity of the TFN membrane amplified, which directly influenced the membrane performance with regards to water flux, salt rejection, and oil rejection. On the other hand, the modified CNC with serine amino acid again enhanced the membrane performance due to additional hydrophilic groups. In GCC countries, as date palm tree (Phoenix dactylifera L.) is the commonly cultivated tree, a significant volume of biowaste is produced each year during the cultivation process [55]. A proper waste extraction is necessary to convert such waste into useful products that are aimed for global reduction of environmental footprints and impacts. Date palm is abundant and rich in cellulosic fibers, and hence it can be used to prepare cellulose and other related products such as CNC [56].
In the current study, the commercial semi hydrophobic polysulphone (PSF) support layer has been used. The CNC incorporated PA layer has been synthesized via in situ interfacial polymerization (IP) process and employed in PW treatment FO process. Due to the PA active layer's vulnerability, TFC membranes are more prone to fouling. Hence this research focused on developing an antifouling, high water flux and less oil flux TFC membrane by incorporating sustainably developed CNC to the PA layer. As nanocellulose has a high surface area, good crystallinity, surface functionalized ability, high aspect ratio, very good chemical resistance, and high Young's modulus [53,57,58], it can help in overcoming the current challenges associated with TFC FO membranes for treating PW.

Materials
A PSF support layer was purchased from Sigma Aldrich, St. Louis, MO, USA. The deionized water (DI), n-hexane, 1,3-phenylenediamine (MPD) (>99%), and trimesoyl chloride (TMC) (>98%) used for the IP process were bought from Merck, Kenilworth, NJ, USA. Sodium hydroxide (NaOH) extra pure pellets and sodium hypochlorite (NaOCl) and sulphuric acid (98%) for the synthesis of CNC were purchased from Sigma Aldrich. The CNC was synthesized from palm tree leaves which were obtained from the Qatar University campus. Further, in FO testing, the synthetic PW was prepared using sodium dioctyl sulfate (SDS) and diesel oil obtained from Sulphur Chemicals Pvt. Lmt Doha Qatar. Isopropyl alcohol (IPA) used for the porosity measurement was obtained from Fisher Scientific, Waltham, MA, USA.

Synthesis of CNC from Palm Tree Leaves
Initially, almost 80 g of leaves were cut into little pieces (10 cm) and soaked in hot water for three hours to remove external impurities (dust, wax). The clean leaf pieces were transferred to an oven with a temperature of 90 • C for 6 h to completely evaporate the water. The dried leaves were then subjected to mechanical treatment (grinding) to transform them into powder (100-200 micrometers). The grinding procedure was used to convert the palm leaves into small fibers, which maximized the efficacy of the chemical treatment, thereby developing a favorable reaction condition by increasing the surface area of the precursor. The obtained fine powder was mixed with NaOH and water in the ratio of 1:2:10 (NaOH:Powder:Water) for alkali treatment. The solution was kept on a magnetic stirrer for 4 h at 70 • C at 1000 rpm. After 4 h of alkali treatment, it was anticipated that the palm leaf's fibrous morphology would inflate and delignify, which was shown by a 27% weight reduction of the fibers. The resultant solution was placed undisturbed for 15 min to settle down the treated powder before being washed 10 times with 100 mL DI water. It was seen that after each wash, the dark brown color of the solution became dull. Additionally, it should be noted that the washing should not halt until the pH of the solution reaches~7. Subsequently, the cellulose microfibrils were collected, bleached with sodium hypochlorite in a ratio of 1.5:1:10 (Sodium Hypochlorite: Powder: DI), and then placed on a magnetic stirrer at 70 • C for 3 h. The white colored microfibrous powder obtained was indeed cellulose at the end of the process. Following that, the cellulose microfibers were washed five times with 100 mL DI water, and it was noted that the whiteness became more prominent with each wash. To prevent the cellulose fibers from denaturing, the drying process should be conducted at 80 • C for 6 h. The obtained cellulose microfibers were gathered and stored in a fridge at 5 • C to avoid the moisture absorption. The cellulose microfibers were then mechanically treated (ball milling for 3 h) to reduce the size of the fibers to nano-level. The produced cellulose nanofibers (5 g) were treated with an acid by the procedure explained by Alothman and team with some modification [59]. Next, hydrolysis was performed in a solution of 40/60 (wt%/wt%) sulfuric/acetic acid containing 5 g of fiber per 100 mL of H 2 SO 4 /C 2 H 4 O 2 solution. The hydrolysis was performed at a temperature of 55 • C for one 90 min so that the acidic reaction could react thoroughly with the fiber. The acidic hydrolyzed fiber mixture was neutralized by centrifugation (5 cycles) and the addition of distilled water to achieve a pH value of 3. The suspension was left afterwards for an hour to permit the undesirable fibers to settle. The supernatant containing CNC was then obtained by decantation. The supernatant was then freeze-dried to produce CNC powder. Figure 2 is the diagrammatic representation for synthesis of cellulose microfibers.
water. The dried leaves were then subjected to mechanical treatment (grinding) to transform them into powder (100-200 micrometers). The grinding procedure was used to convert the palm leaves into small fibers, which maximized the efficacy of the chemical treatment, thereby developing a favorable reaction condition by increasing the surface area of the precursor. The obtained fine powder was mixed with NaOH and water in the ratio of 1:2:10 (NaOH:Powder:Water) for alkali treatment. The solution was kept on a magnetic stirrer for 4 h at 70 °C at 1000 rpm. After 4 h of alkali treatment, it was anticipated that the palm leaf's fibrous morphology would inflate and delignify, which was shown by a 27% weight reduction of the fibers. The resultant solution was placed undisturbed for 15 min to settle down the treated powder before being washed 10 times with 100 mL DI water. It was seen that after each wash, the dark brown color of the solution became dull. Additionally, it should be noted that the washing should not halt until the pH of the solution reaches ~7. Subsequently, the cellulose microfibrils were collected, bleached with sodium hypochlorite in a ratio of 1.5:1:10 (Sodium Hypochlorite: Powder: DI), and then placed on a magnetic stirrer at 70 °C for 3 h. The white colored microfibrous powder obtained was indeed cellulose at the end of the process. Following that, the cellulose microfibers were washed five times with 100 mL DI water, and it was noted that the whiteness became more prominent with each wash. To prevent the cellulose fibers from denaturing, the drying process should be conducted at 80 °C for 6 h. The obtained cellulose microfibers were gathered and stored in a fridge at 5 °C to avoid the moisture absorption. The cellulose microfibers were then mechanically treated (ball milling for 3 h) to reduce the size of the fibers to nano-level. The produced cellulose nanofibers (5 g) were treated with an acid by the procedure explained by Alothman and team with some modification [59]. Next, hydrolysis was performed in a solution of 40/60 (wt%/wt%) sulfuric/acetic acid containing 5 g of fiber per 100 mL of H2SO4/C2H4O2 solution. The hydrolysis was performed at a temperature of 55 °C for one 90 min so that the acidic reaction could react thoroughly with the fiber. The acidic hydrolyzed fiber mixture was neutralized by centrifugation (5 cycles) and the addition of distilled water to achieve a pH value of 3. The suspension was left afterwards for an hour to permit the undesirable fibers to settle. The supernatant containing CNC was then obtained by decantation. The supernatant was then freeze-dried to produce CNC powder. Figure 2 is the diagrammatic representation for synthesis of cellulose microfibers.

Developing the Membrane
To prepare the TFC membrane, the PSF which was used as the support was submerged initially in distilled water for at least 6 h. Subsequently, the PA layer on top of a PSF support was developed via an IP process. The membrane support was immersed in a 1 wt.% MPD/distilled water aqueous solution for 10 min, after which a synthetic rubber roller was utilized for the elimination of the surplus solution from the membrane surface. Subsequently, a 0.15 wt.% TMC-hexane solution was drained over the membrane cover for 120 s. After being exposed to air for 60 s, drying in an oven for one minute at 55 °C, and lastly being stored in deionized water. As a result, PA layer was developed on the top of the PSF support to develop a TFC membrane.
Using the identical method as for the preparation of TFC membrane, the TFN membranes were developed ( Figure 3) by mixing MPD aqueous solution with CNC at four

Developing the Membrane
To prepare the TFC membrane, the PSF which was used as the support was submerged initially in distilled water for at least 6 h. Subsequently, the PA layer on top of a PSF support was developed via an IP process. The membrane support was immersed in a 1 wt.% MPD/distilled water aqueous solution for 10 min, after which a synthetic rubber roller was utilized for the elimination of the surplus solution from the membrane surface. Subsequently, a 0.15 wt.% TMC-hexane solution was drained over the membrane cover for 120 s. After being exposed to air for 60 s, drying in an oven for one minute at 55 • C, and lastly being stored in deionized water. As a result, PA layer was developed on the top of the PSF support to develop a TFC membrane.
Using the identical method as for the preparation of TFC membrane, the TFN membranes were developed ( Figure 3) by mixing MPD aqueous solution with CNC at four different concentrations (0.01 wt.%, 0.03 wt.%, 0.05 wt.%, and 0.07 wt.%). The subsequent preparation process of TFM membrane stayed similar to the TFC membrane. Table 1 shows the nomenclature of the different TFN membranes developed.

Characterization of the Developed Cellulose Nanocrystals and Modified Membranes
CNC was characterized to verify that the nanomaterial was successfully synthesized and the characterization of both the TFC and TFN membranes was performed for examining the IP process's impact on the membrane after nanomaterial incorporation. The FTIR (760 Nicolet) was employed for identifying the appropriate organic and inorganic peaks present in the specimen. The morphology of the CNC was examined using transmission electron microscopy (TEM) (HT 770, Hitachi, Tokyo, Japan). To understand the crystalline nature of synthesized CNC, the X-ray diffraction (Rigaku. Miniflex2 Desktop, Tokyo, Japan) was employed. The Raman Microscope Thermo Fisher Scientific DXR was the instrument used for Raman spectroscopy. The Nova Nano SEM 450 scanning electron microscope (SEM) was employed in this study for membrane characterization, and its voltage capacity ranged from 200 V-30 kV. SEM analysis was utilized to describe the surface of the membranes. For examining the surface roughness of modified and unmodified membrane specimens, a Veeco Metrology Nasoscope IV 3100 SPM has been employed. For validating the formation of the selective layer and the efficient inclusion of CNC into the TFC membranes, FTIR (760 Nicolet) analysis was carried out. The contact angle system OCA (708381-T, LMS Scientific, Selangor, Malaysia) was applied to determine the membrane's hydrophilicity. Conductivity measurements were determined using an 856 conductivity module (Metrohm, Switzerland).

Characterization of the Developed Cellulose Nanocrystals and Modified Membranes
CNC was characterized to verify that the nanomaterial was successfully synthesized and the characterization of both the TFC and TFN membranes was performed for examining the IP process's impact on the membrane after nanomaterial incorporation. The FTIR (760 Nicolet) was employed for identifying the appropriate organic and inorganic peaks present in the specimen. The morphology of the CNC was examined using transmission electron microscopy (TEM) (HT 770, Hitachi, Tokyo, Japan). To understand the crystalline nature of synthesized CNC, the X-ray diffraction (Rigaku. Miniflex2 Desktop, Tokyo, Japan) was employed. The Raman Microscope Thermo Fisher Scientific DXR was the instrument used for Raman spectroscopy. The Nova Nano SEM 450 scanning electron microscope (SEM) was employed in this study for membrane characterization, and its voltage capacity ranged from 200 V-30 kV. SEM analysis was utilized to describe the surface of the membranes. For examining the surface roughness of modified and unmodified membrane specimens, a Veeco Metrology Nasoscope IV 3100 SPM has been employed. For validating the formation of the selective layer and the efficient inclusion of CNC into the TFC membranes, FTIR (760 Nicolet) analysis was carried out. The contact angle system OCA (708381-T, LMS Scientific, Selangor, Malaysia) was applied to determine the membrane's hydrophilicity. Conductivity measurements were determined using an 856 conductivity module (Metrohm, Switzerland).

Preparation of Synthetic PW
Synthetic PW was prepared as stated by Lee and team [32] by mixing 9 parts SDS (emulsifying agent) to 1 part diesel oil to develop an oil-in-water emulsion (Figure 4), which was then homogenized with a magnetic stirrer. Finally, the mix was sonicated for 10 min in an ice bath employing a Hielscher ultrasonic processor (Hielscher UP400s, Teltow, Germany) to develop synthetic PW.

Preparation of Synthetic PW
Synthetic PW was prepared as stated by Lee and team [32] by mixing 9 parts SDS (emulsifying agent) to 1 part diesel oil to develop an oil-in-water emulsion (Figure 4), which was then homogenized with a magnetic stirrer. Finally, the mix was sonicated for 10 min in an ice bath employing a Hielscher ultrasonic processor (Hielscher UP400s, Teltow, Germany) to develop synthetic PW.

Membrane Porosity, Thickness
Using the gravimetric approach, the porosity of the TFC and TFN membranes was established. Initially, the membrane was submerged in 100% IPA for 1 day in order to saturate the porous structure with IPA and remove any internal water and air. The membrane was carefully switched from IPA to 50% (v/v) IPA for an additional 24 h. The membrane was weighed and dried for 1 day at ambient temperature. Then, dried membrane's weight was calculated. The membrane porosity ( ) was determined using the Formula (1) where ω1 is the weight of the IPA wetted membrane, ω2 is the weight of dried membrane, ρi is the density of the IPA, and ρp is the density of the polymer. In addition, the membrane thickness was calculated using a micrometer.

Pure Water Permeability (A), Salt Permeability (B), Salt Rejection (Rs, %) and Oil Rejection (Ro, %)
The water permeability (A, LMHB), salt rejection (Rs, %), salt permeability (B, LMH), and oil rejection (Ro, %) of the membranes were defined by testing the membranes employing a lab-scale dead-end filtration RO system. The research was conducted by the experiments being at ambient temperature with a membrane active area of 0.0042 m 2 . Under a pressure of 5 bar, the A values have been determined by running experimentations using DI water as feed solution. The next step included collecting 5 mL of water at regular intervals and noting the duration. The experiment was done three times, and the average result was reported. The A value was calculated using Equation (2) where, Am denotes the membrane effective area (0.00146 m 2 ), V equals permeate volume (mL), ∆P is the applied pressure difference (bar), and ∆t is the operating duration (h), Salt

Membrane Porosity, Thickness
Using the gravimetric approach, the porosity of the TFC and TFN membranes was established. Initially, the membrane was submerged in 100% IPA for 1 day in order to saturate the porous structure with IPA and remove any internal water and air. The membrane was carefully switched from IPA to 50% (v/v) IPA for an additional 24 h. The membrane was weighed and dried for 1 day at ambient temperature. Then, dried membrane's weight was calculated. The membrane porosity (ε) was determined using the Formula (1) where ω 1 is the weight of the IPA wetted membrane, ω 2 is the weight of dried membrane, ρ i is the density of the IPA, and ρ p is the density of the polymer. In addition, the membrane thickness was calculated using a micrometer. The water permeability (A, LMHB), salt rejection (R s , %), salt permeability (B, LMH), and oil rejection (R o , %) of the membranes were defined by testing the membranes employing a lab-scale dead-end filtration RO system. The research was conducted by the experiments being at ambient temperature with a membrane active area of 0.0042 m 2 . Under a pressure of 5 bar, the A values have been determined by running experimentations using DI water as feed solution. The next step included collecting 5 mL of water at regular intervals and noting the duration. The experiment was done three times, and the average result was reported. The A value was calculated using Equation (2) where, A m denotes the membrane effective area (0.00146 m 2 ), V equals permeate volume (mL), ∆P is the applied pressure difference (bar), and ∆t is the operating duration (h), Salt rejection (R s ) values were established by performing the tests using a 2000 ppm NaCl solution as the feed under a transmembrane pressure of 5 bar. An amount of 5 mL of salt permeate was collected and the time needed was documented. This process was repeated three times to obtain an average reading. R s was calculated as per Equation (3): where C p is the NaCl concentration of the permeate and C f is the feed NaCl concentration. These values were calculated by using the conductivity of the feed and the draw solutions. The salt permeability (B) values of membranes were defined using the solutiondiffusion principle as per Equation (4): where A m is the active area of the membrane (0.00146 m 2 ), ∆π is the osmotic pressure difference and ∆P is applied pressure difference. The experiments with 20,000 ppm oil-water emulsion as the feed under a transmembrane pressure of 2 bar were used to calculate the R o values. Oil rejection can be discovered in a variety of ways, such as using a UV-vis spectrometer or a TOC analyzer. The concentrations of the oil feed and permeate were obtained using a UV-vis spectrometer (DR2800, Hach) in order to obtain the oil rejection because utilizing a TOC analyzer takes more time. The absorbance was being measured at 270 nm, the wavelength at which the absorbance peaked.
R o was calculated as per the Equation (5): where C po and C fo represents oil permeate concentration and oil feed concentration, respectively.

FO Setup and Experiment (Water Flux, Reverse Salt Flux, Oil Flux)
As demonstrated in a prior work [7], FO experiments were performed on a crossflow forward osmosis device at lab scale. The effective membrane area in the crossflow FO cell was measured to be 0.00146 m 2 , and the system operating pressure during the process for DS and FS circulation with two variable speed pumps was observed to be 1 bar. All experiments were conducted at room temperature (22 • C). Active layer facing draw solution (AL-DS) was the membrane orientation, and 32.72 cm/s was used for the FS and DS speeds. The FS was 6000 ppm of greasy wastewater while the DS was 2.0 M of concentrated salt solution. A computerized weight balance was located at the bottom of the FS tank and was used to determine the precise water flux. An amount of 500 mL/min of cross-flow was used to circulate both FS and DS. Figure 5 depicts the configuration of the FO system used in this study.  When the system was in operation, a draw solution (2M NaCl) and a feed solution (6000 ppm) cycled counter-currently on either side of the membrane. The FO mode, in which the active layer is up against the feed solution, was used to test the membranes. Water flux (J v , LMH), reverse salt flux (J s , gMH), and oil flux (J o , gMH), which were computed using Equations (6)-(8), respectively, were used to calculate membrane performance: where A eff is the effective membrane surface area (m 2 ), ∆V (L) is the water volume that has permeated across the membrane in a fixed time ∆t (h) at the time of the test. C tf and V tf are the salt concentration (g/L) and the feed volume (L) at the end of FO tests, respectively. C td and V td are the oil concentration (g/L) and the volume of the draw (L) at the end of FO tests, respectively. Using a UV-vis spectrometer (UV Biochrom Spectrophotometer) with a wavelength of 270 nm, the amount of oil in the DS was determined.

Forward Osmosis Experimental Results Validation
Kim and his colleagues [60] described a step-by-step process for creating a prediction model for scaling up forward osmosis in their study. When compared to the lumped parameter model prediction in the 15 • C to 35 • C temperature range, the stepwise model prediction in their work indicated a good agreement with experimental data of salt flux and water flux. The study's findings demonstrated the advantages of using a stepwise model to forecast water flux. In the current work, certain empirical parameters in the stepwise model have been modified for specifying the osmotic pressure as well as for estimating the impact of various membrane parameters (tortuosity, porosity, salt permeability water permeability, and salt rejection).

FTIR Analysis
The FTIR spectra of developed CNC and cellulose is shown in Figure 6. It should be noted that the FTIR spectra of the CNC produced and the cellulose were quite comparable. This demonstrated that no new bonds are formed during the acid hydrolysis of cellulose. The O-H bending corresponded to the spectral bands of CNC and cellulose at about 3402 cm −1 . The C-H group, on the other hand, is responsible for the band at about 2394 cm −1 , and the C-O bending of pure cellulose and CNC is responsible for the band at almost 1065 cm −1 . Moreover, the cellulosic beta glycosidic linkages are associated with the bands at almost 890 cm −1 . The C-O-C pyranose ring is responsible for the peak at almost 1050 cm −1 , and the band at 908 cm −1 is connected to the glycosidic connections between the glucose units in the cellulose II framework. The cellulose and CNC FTIR results are consistent with the cellulose and CNC FTIR spectrum created by Thakur et al. [61], where the CNC was created from rice straw. cm −1 . The C-H group, on the other hand, is responsible for the band at about 2394 cm −1 , and the C-O bending of pure cellulose and CNC is responsible for the band at almost 1065 cm −1 . Moreover, the cellulosic beta glycosidic linkages are associated with the bands at almost 890 cm −1 . The C-O-C pyranose ring is responsible for the peak at almost 1050 cm −1 , and the band at 908 cm −1 is connected to the glycosidic connections between the glucose units in the cellulose II framework. The cellulose and CNC FTIR results are consistent with the cellulose and CNC FTIR spectrum created by Thakur et al. [61], where the CNC was created from rice straw.

XRD Analysis
The crystalline behavior as well as the relationship between the properties and crystal structure are studied using the XRD analysis. Because cellulose's molecular structure is both amorphous and crystalline, the crystalline sections of the cellulose chains are kept together by mutual hydrogen bonds, whereas the amorphous regions of the cellulosic chains do not have any hydrogen bonds. The mechanical and chemical processes have an impact on the crystallite size as well as the crystallinity of the cellulose. Figure 7 shows the CNC and cellulose XRD diffraction pattern. The samples had peaks that were consistent with the unique peaks of the cellulose framework at 2 h = 16.6 and 22.4 as well as 34.5 at the (1 1 0), (2 0 0), and (0 0 4) planes, respectively. According to the amorphous subtraction approach, the crystallinity index was found to be 61.3% for cellulose and 75.5% for CNCs. At the period of cellulose acid hydrolysis, the crystallinity index increases. The cellulose and CNC XRD results are comparable to the cellulose and CNC XRD spectra created by Thakur et al. [61].

XRD Analysis
The crystalline behavior as well as the relationship between the properties and crystal structure are studied using the XRD analysis. Because cellulose's molecular structure is both amorphous and crystalline, the crystalline sections of the cellulose chains are kept together by mutual hydrogen bonds, whereas the amorphous regions of the cellulosic chains do not have any hydrogen bonds. The mechanical and chemical processes have an impact on the crystallite size as well as the crystallinity of the cellulose. Figure 7 shows the CNC and cellulose XRD diffraction pattern. The samples had peaks that were consistent with the unique peaks of the cellulose framework at 2 h = 16.6 and 22.4 as well as 34.5 at the (1 1 0), (2 0 0), and (0 0 4) planes, respectively. According to the amorphous subtraction approach, the crystallinity index was found to be 61.3% for cellulose and 75.5% for CNCs. At the period of cellulose acid hydrolysis, the crystallinity index increases. The cellulose and CNC XRD results are comparable to the cellulose and CNC XRD spectra created by Thakur et al. [61].

TEM Analysis
After ball milling and acid treatment, the CNC looks spherical in the TEM picture. The TEM images of cellulose nanocrystals that were treated with ball milling are shown in Figure 8a,b, respectively. The TEM images of acid-treated cellulose nanocrystals are shown in Figure 8c,d, respectively. It was shown that the CNC was only slightly aggregated, with a few particles clustering together in groups. The dimensions of cellulose nan-

TEM Analysis
After ball milling and acid treatment, the CNC looks spherical in the TEM picture. The TEM images of cellulose nanocrystals that were treated with ball milling are shown in Figure 8a,b, respectively. The TEM images of acid-treated cellulose nanocrystals are shown in Figure 8c,d, respectively. It was shown that the CNC was only slightly aggregated, with a few particles clustering together in groups. The dimensions of cellulose nanofibers and CNC were somewhere in the 78-100 nm range. Generally, the structure of nanocellulose is determined by the conditions of acid hydrolysis as well as the source of the fiber. The structure of nanocellulose usually resembles that of a diamond crystal, but in this instance, the form appeared to be different. The ball milling effect, which breaks down the fundamental structure of nanocellulose, is the most reasonable scenario due to the changes of different shapes. The surface of the CNC formed from palm tree leaves is often coarser due to the presence of sharp edges, which might make a contribution to the formation of fouling. As compared with previous findings that were reported using the same concentration of CNC, the produced CNC do not have any jagged corners, which is still another explanation for the smooth surface combined with good nanomaterial distribution. Some examples of innovative research include the investigation of how the nanocrystal structure of cellulose is affected by a variety of mechanical processes. Researchers Agustin et al. [62], Jewan et al. [63], and Mehanny [64] found that garlic stems and palm tree leaves both produced relatively similar types of nanocellulose.

FTIR Analysis
The FTIR spectra of TFC as well as many distinct TFN membrane modifications are shown in Figure 9. At a frequency of 1645 cm −1 , aromatic ring stretching, also known as amide II, appeared in all TFC membranes. This demonstrated that the development of the selective polyamide layer was effective. In addition, the absorption peaks that occur at roughly 1290 cm −1 and 1150 cm −1 are linked to the symmetrical bending vibrations that occur in the

FTIR Analysis
The FTIR spectra of TFC as well as many distinct TFN membrane modifications are shown in Figure 9. At a frequency of 1645 cm −1 , aromatic ring stretching, also known as amide II, appeared in all TFC membranes. This demonstrated that the development of the selective polyamide layer was effective. In addition, the absorption peaks that occur at roughly 1290 cm −1 and 1150 cm −1 are linked to the symmetrical bending vibrations that occur in the O=S=O group [65]. Moreover, the peaks at 1495 cm −1 and 1580 cm −1 represent distinct absorption bands of C-C stretching vibration for benzenoid rings and bands of C=C bonds for aromatic rings, respectively [59]. After incorporating CNCs in the PA layer, the spectra of all produced membranes displayed peaks at 3200 cm −1 and at 3500 cm −1 linked with the stretching of −OH groups [66]. The ATR-FITR examination of the membranes, as a result, provided conclusive evidence that CNCs are present in the TFN membranes.

AFM Results
It can be observed from the findings of the AFM (Figure 10) that the surface roughness of the membranes decreased with a given CNC dosage and then increased. This indicates the morphological structure of the TFN and TFC membranes and demonstrates the amount of polymerization. This is partly related to the various concentrations of CNC that were used as well as a variation in the rate of the reaction of MPD and TMC as a result of the nanomaterial loadings [67]. The many hydroxyl groups of CNCs react with the acyl chloride group in TMC to produce ester linkages, which change the efficiency of interfacial polymerization between MPD and TMC [68]. This occurs because CNCs contain a large number of acyl chloride groups. The preparation of the polyamide layer is modified when CNCs are added, which in turn results in an alteration in the surface morphology of the TFN membranes, which have the potential to affect how well the membranes perform. The data obtained from the AFM demonstrate that, with the exception of TFN-7, all of the other unmodified and modified membranes (TFC, TFN-1, and TFN-5) maintain a thick and homogenous polyamide layer. As a result of the significant loading of CNC nanomaterials, this indicates that the degree of crosslinking was high for all of the membranes with the exception of TFN-7. These observations have an indirect and direct connection on the performance of the membrane (flux and rejections). The root mean square (RMS) roughness is one of the characteristics for membrane surface topographies that is mentioned most often in the literature. The standard deviation of the pixel height data may be thought of as the RMS roughness, which can also be thought of as the divergence

AFM Results
It can be observed from the findings of the AFM (Figure 10) that the surface roughness of the membranes decreased with a given CNC dosage and then increased. This indicates the morphological structure of the TFN and TFC membranes and demonstrates the amount of polymerization. This is partly related to the various concentrations of CNC that were used as well as a variation in the rate of the reaction of MPD and TMC as a result of the nanomaterial loadings [67]. The many hydroxyl groups of CNCs react with the acyl chloride group in TMC to produce ester linkages, which change the efficiency of interfacial polymerization between MPD and TMC [68]. This occurs because CNCs contain a large number of acyl chloride groups. The preparation of the polyamide layer is modified when CNCs are added, which in turn results in an alteration in the surface morphology of the TFN membranes, which have the potential to affect how well the membranes perform. The data obtained from the AFM demonstrate that, with the exception of TFN-7, all of the other unmodified and modified membranes (TFC, TFN-1, and TFN-5) maintain a thick and homogenous polyamide layer. As a result of the significant loading of CNC nanomaterials, this indicates that the degree of crosslinking was high for all of the membranes with the exception of TFN-7. These observations have an indirect and direct connection on the performance of the membrane (flux and rejections). The root mean square (RMS) roughness is one of the characteristics for membrane surface topographies that is mentioned most often in the literature. The standard deviation of the pixel height data may be thought of as the RMS roughness, which can also be thought of as the divergence of the peaks and valleys from the mean plane. The modified TFN-1,5,7 membranes each had an RMS value of 44.05 nm, 31.76 nm, and 95.88 nm, correspondingly. These figures make it very evident that the CNC has been very well integrated. Although a rougher active surface has better water permeability due to its larger surface area in contact with water, it is also more likely to become fouled because there are more possibilities for emulsified oil particles to come into contact with the large membrane surface [69]. The above makes it more likely that the membrane will become clogged. When there is a greater level of surface roughness, it is quicker for particles of a contaminant to adhere to the surface of the membrane. Therefore, membranes with a higher surface roughness experience a greater amount of fouling and a more rapid decrease in flow. As compared to the unmodified TFC membrane, the data suggest that the integration of CNC into the PA layer (TFN-1 and TFN-5) results in a reduction in the surface roughness. It was also determined that the presence of CNC nanoparticles in the proper number results in the formation of a layer that is compact, dense, and smooth, which will provide an environment that is unfavorable for the attachment of oil. The rougher the membrane, the more crests and valleys it will have. This will allow for a greater interaction with the water droplets, which will then lead to the formation of a dense and uniform hydration layer, which will increase the water flux and oil rejection because oil molecules are hydrophobic [44]. greater amount of fouling and a more rapid decrease in flow. As compared to the unmodified TFC membrane, the data suggest that the integration of CNC into the PA layer (TFN-1 and TFN-5) results in a reduction in the surface roughness. It was also determined that the presence of CNC nanoparticles in the proper number results in the formation of a layer that is compact, dense, and smooth, which will provide an environment that is unfavorable for the attachment of oil. The rougher the membrane, the more crests and valleys it will have. This will allow for a greater interaction with the water droplets, which will then lead to the formation of a dense and uniform hydration layer, which will increase the water flux and oil rejection because oil molecules are hydrophobic [44].

Contact Angle Analysis
The developed membranes of contact angles are shown in the Table 2. The research demonstrated that all membranes are hydrophilic; however, the polyamide membrane coupled with cellulose nanocrystals was less hydrophobic than the other membranes. The data from the FT-IR spectrometer indicate that this is most likely due to the presence of hydroxyl -OH groups in the CNC-modified membrane. The hydrophilicity of the membranes and their roughness are shown to have a correlation with one another. The unmodified membrane with decreased roughness has a higher contact angle in contrast to the CNC-modified membrane, which exhibits a lower contact angle due to the membrane's increased roughness. Therefore, enhanced hydrophilicity, but at the same time, the surge displayed by the TFN-7 membrane in regard to the roughness of the surface, provided evidence of irregular polymerization and agglomeration of CNCs, which led in relatively high oil and salt flow.

Contact Angle Analysis
The developed membranes of contact angles are shown in the Table 2. The research demonstrated that all membranes are hydrophilic; however, the polyamide membrane coupled with cellulose nanocrystals was less hydrophobic than the other membranes. The data from the FT-IR spectrometer indicate that this is most likely due to the presence of hydroxyl -OH groups in the CNC-modified membrane. The hydrophilicity of the membranes and their roughness are shown to have a correlation with one another. The unmodified membrane with decreased roughness has a higher contact angle in contrast to the CNC-modified membrane, which exhibits a lower contact angle due to the membrane's increased roughness. Therefore, enhanced hydrophilicity, but at the same time, the surge displayed by the TFN-7 membrane in regard to the roughness of the surface, provided evidence of irregular polymerization and agglomeration of CNCs, which led in relatively high oil and salt flow.

SEM Analysis of Different Membranes
The corresponding SEM pictures of the produced membranes are shown in Figure 11. As a result of a high concentration of CNC in the PA layer, there was irregular dispersion and clustering, which resulted in a rougher PA layer deposition in membrane. This can be observed in Figure 11 and is confirmed by the data obtained from the AFM. Therefore, it is clear that raising the concentration does not instantaneously result in improved performance. Rather, the key to producing an optimum membrane that performs at its greatest potential is to strike a balance between the concentrations of the different components. On the other hand, the SEM picture obtained from TFN-5 indicated that the nanomaterials were distributed evenly across the skin layer, with certain CNC particles showing a false similarity to one another.

SEM Analysis of Different Membranes
The corresponding SEM pictures of the produced membranes are shown in Figure  11. As a result of a high concentration of CNC in the PA layer, there was irregular dispersion and clustering, which resulted in a rougher PA layer deposition in membrane. This can be observed in Figure 11 and is confirmed by the data obtained from the AFM. Therefore, it is clear that raising the concentration does not instantaneously result in improved performance. Rather, the key to producing an optimum membrane that performs at its greatest potential is to strike a balance between the concentrations of the different components. On the other hand, the SEM picture obtained from TFN-5 indicated that the nanomaterials were distributed evenly across the skin layer, with certain CNC particles showing a false similarity to one another.

Permeability and Rejections
The permeability and rejection tests were carried out using a set up that consisted of a RO dead end. The water permeability and salt permeability of TFC and TFN membranes are shown in Figure 12a. TFN-1 has 0.01 weight percent CNC in the PA layer, TFN-5 has 0.05 weight percent CNC in the PA layer, and TFN-7 has 0.07 weight percent CNC in the PA layer. When contrasted with the TFC and the other TFN membranes, it was discovered that the TFN-7 membrane has the greatest permeability coefficients for both pure water and salt.

Permeability and Rejections
The permeability and rejection tests were carried out using a set up that consisted of a RO dead end. The water permeability and salt permeability of TFC and TFN membranes are shown in Figure 12a. TFN-1 has 0.01 weight percent CNC in the PA layer, TFN-5 has 0.05 weight percent CNC in the PA layer, and TFN-7 has 0.07 weight percent CNC in the PA layer. When contrasted with the TFC and the other TFN membranes, it was discovered that the TFN-7 membrane has the greatest permeability coefficients for both pure water and salt. Both the water permeability and salt permeability readings were at 2.72 LMHB, whereas the salt permeability value was 2.12 LMH. On the contrary, the permeability values of the TFC, TFN-1, and TFN-5 membranes were lower than those of the TFN-7 membrane. These membranes showed values of 0.460, 1.420, and 1.61 LMHB pure water permeability (A), and 0.41, 1.24, and 1.42 LHM salt permeability (B), respectively. The phenomenon could be explained by the increased OH groups of the CNCs interacting with the increased TMC to produce an increased level of crosslinking in the selective layer of the CNC-TFC membranes. As a consequence, the membranes were able to reject more salt [70]. When the concentration of CNCs was raised to 0.07 weight percent, there was a noticeable improvement in the membrane's flow compared to that of the uncontaminated TFC membrane. The increased flow of the membrane may be attributed to a combination of factors, including increased hydrophilicity, increased surface functional groups, and increased density of the polyamide layer. The increased surface hydrophilicity causes the membrane's water flow to rise [71]. This is due to the stronger affinity for water, which is caused by the improved surface hydrophilicity. The presence of high-polar groups, such as -COO-, -NH 2 , and -OH on the surface of the membrane, as well as an abundance of -COO-and -OH groups on the surfaces of CNC nanoparticles, [72] contributes to an increase in surface hydrophilicity and a corresponding acceleration in the movement of water molecules. In addition, water molecules are able to travel via the interfacial gaps that exist between CNCs and the polyamide that has CNCs included in it. A passage such as this one would effectively lower the nominal diameter of the dense barrier layer of the TFC membrane, which would ultimately result in an increase in the water flow over the membrane.
Upon analyzing the levels of salt rejection (shown in Figure 12b) and oil rejection (shown in Figure 12c), it is possible to see that the TFC, TFN-1, and TFN-5 membranes all displayed greater levels of salt rejection and oil rejection, respectively. The pristine TFC membrane had a salt rejection rate of 96.2% and an oil rejection rate of 90.5%. In comparison, the TFN-1 and TFN-5 membranes had a salt rejection rate of 96.8% and 99.0%, respectively, while they had an oil rejection rate of 95.34% and 97.45%. The TFN-7 membrane, on the other hand, exhibited a lower level of rejection, which came in at 95.80% for salt and 91.22% for oil, respectively. TFN-5 showed the least deviation between simulated and experimental (salt and oil rejection data) among all TFC and TFN membranes (Figure 12b), with values of 0.4% (salt rejection) and 2.0% (oil rejection). In contrast, TFN-7 shows the highest deviation, with values of 3.68% (salt rejection) and 8.0% (oil rejection) (oil rejection). A subsequent investigation found that the heavy loading of the CNC had a detrimental effect on the growth of the thin-film PA layer, which was the primary target of the investigation. It is likely that the poor performance of TFN-7 was caused by the spontaneous, non-uniform porosity distribution throughout the surface of the membrane, as well as the uneven microporous distribution caused by the inclusion of 0.07 weight percent. Throughout the period of the interfacial polymerization process, CNC had a significant influence on the TMC and MPD polymerization occurring on the substrate. As a result, a polyamide layer with defects was produced, as seen by the scanning electron micrograph. The reduction in salt rejection was probably caused by an overloading of CNCs in the polyamide layer, which resulted in a loose structure for the polyamide material. In order to avoid the unfavorable trade-off effect that occurs during the production of the TFN-7 membrane, an adequate concentration of CNC should be used throughout this stage of the process, exactly like the formation of the TFN-1 and TFN-5 membranes. CNC is in a high concentration in the TFN-7 membrane and showed a high reverse solute flux (0.90 GMH experimental, 0.83 GMH simulated with deviation of 7.44%) and oil flux (0.00423 GMH experimental, 0.00485 GMH simulated with deviation 12.78%) as compared to TFC and other TFN membranes. This is because of a poor degree of cross-linked PA layer formation due to the high concentration of CNC, because oil rejection and salt rejection require a nicely uniform PA layer, which resists the permeation of salt and oil [72]. Due to the distorted active layer, the salt and oil flux was high. On the other hand, the TFN-5 was showing higher water flux with a higher salt and oil rejection with a lesser deviation in experimental and simulated data (30.57 LMH experimental,30.08 LMH simulated with 1.65% of deviation). The reverse salt flux and oil flux (0.57 GMH experimental, 0.55 GMH simulated with 3.83% deviation (reverse salt flux) and 0.00754 GMH experimental, 0.00795 GMH with minimum deviation of 5.16%) are noted. The reason for high flux, salt, and oil rejection of TFN-5 was primarily the uniform dispersion of CNC with the PA layer, which allows the water molecules to interact with the inductively activated cellulose nanocrystal molecules to form a dense water layer, as water molecules [67]. The density of OH groups on the polyamide membrane is increased by the cellulose nanocrystal, increasing the membrane's hydrophilicity. The proper dispersion of CNC into the PA layer allows a uniform pore formation condition. In addition, the internal concentration polarization of the TFN-5 membrane was also decreased, which could be due to its increased oil flux relative to other membranes. This is because of the increased deposition of solutes on pristine TFC and TFN membrane's porous support layer, which resulted in increased internal concentration polarization, hence causing reduced water flux relative to TFN-7. CNC is in a high concentration in the TFN-7 membrane and showed a high reverse solute flux (0.90 GMH experimental, 0.83 GMH simulated with deviation of 7.44%) and oil flux (0.00423 GMH experimental, 0.00485 GMH simulated with deviation 12.78%) as compared to TFC and other TFN membranes. This is because of a poor degree of cross-linked PA layer formation due to the high concentration of CNC, because oil rejection and salt rejection require a nicely uniform PA layer, which resists the permeation of salt and oil [72]. Due to the distorted active layer, the salt and oil flux was high. On the other hand, the TFN-5 was showing higher water flux with a higher salt and oil rejection with a lesser deviation in experimental and simulated data (30.57 LMH experimental, 30.08 LMH simulated with 1.65% of deviation). The reverse salt flux and oil flux (0.57 GMH experimental, 0.55 GMH simulated with 3.83% deviation (reverse salt flux) and 0.00754 GMH experimental, 0.00795 GMH with minimum deviation of 5.16%) are noted. The reason for high flux, salt, and oil rejection of TFN-5 was primarily the uniform dispersion of CNC with the PA layer, which allows the water molecules to interact with the inductively activated cellulose nanocrystal molecules to form a dense water layer, as water molecules [67]. The density of OH groups on the polyamide membrane is increased by the cellulose nanocrystal, increasing the membrane's hydrophilicity. The proper dispersion of CNC into the PA layer allows a uniform pore formation condition. In addition, the internal concentration polarization of the TFN-5 membrane was also decreased, which could be due to its increased oil flux relative to other membranes. This is because of the increased deposition of solutes on pristine TFC and TFN membrane's porous support layer, which resulted in increased internal concentration polarization, hence causing reduced water flux relative to TFN-7.
The hydrophilicity of cellulose nanocrystal plays the most important and dominant role in the performance of all modified membranes [73]. To generate flat sheets with CH-O hydrogen bonds, cellulose chains are joined together by OH-O-type hydrogen bonds. These interactions involve nonbonding forces, including electrostatic, hydrogen bonding, and van der Waals forces. Here, cellulose nanocrystals interact strongly with water because of its hydrophilic nature. Nevertheless, the intermolecular hydrogen bond losses within the chains of cellulose are replaced by new hydrogen bonds created by water molecules during the water cellulose contact. The glycosidic linkages in the cellulose molecule are surrounded by substantial anti-bonding electron clouds. The approach of the water molecules induces a polarization in these anti-bonding electron cloud structures and an electrostatic dipole can be produced by distorting electron clouds. The concept of polarizability results in the development of a wave dipole. The interactions are dominated and defined by the characteristics of the hydrocarbon chains. The Pauli Principle's repulsion component prevents the chains from collapsing. There could be a variety of interactions, including attractive or repulsive interactions between water molecules and permanent dipoles found in cellulose polymers, induction interactions between permanent water molecule poles and induced multipoles found in cellulose chains, and any pairs of molecules resulting from interactions on instantaneous multi-poles [73]. The reason disused here is valid for all the TFN membranes but the contradiction between TFN-7 and TFN-5 membrane was generated when it comes to the salt and oil rejection efficiency, which is the main aim of the research; the lower salt and oil flux of TFN-5 membrane set a threshold point with respect to concentration of CNC.
According to the solution-diffusion theory, the FO solute flux is another essential FO parameter that is proportional to the concentration difference across the membranes. For realistic FO processes, membranes with minimal solute flux are preferred [54]. Comparing the solute flux through the CNC-nanoparticle-incorporated TFN membranes to the control TFC membrane, there was a negligible increase noted. Because of the lower PA crosslinking level, TFN-7 with the maximum CNC loading showed the largest solute flux. Since the membranes used in FO operations should have high water flux and low solute flux at the same time, it was determined that CNC loading beyond 0.05 wt% was harmful for FO applications. Since the solute flux is proportional to the salt rejection according to the solution-diffusion theory, the trend was consistent with the salt rejection reported in RO experiments [74].

Sustainable Methods for Draw Solution Treatment
As it has been observed that the membrane is not giving 100% oil rejection, which pollutes the draw solution and again causes a major issue at a larger scale, some sustainable methods can be used to treat the draw solution, as the concentration of oil in the draw solution is very low.

1.
Bioremediation: Utilizing microorganisms, such as bacteria, fungi, or algae, to break down and metabolize the oil. These microorganisms can be added to the draw solution, or one can promote the growth of indigenous microorganisms by adding nutrients like nitrogen and phosphorus. This method may take longer than other approaches but is more environmentally friendly.

2.
Oleophilic materials: To remove the oil from the draw solution, oleophilic materials like oil-absorbent pads, sheets, or booms can be used. Most of these materials are hydrophobic, which means they repel water and prefer to attract oil. Once the oil has been absorbed, the oleophilic materials can be taken out and either regenerated or replaced.

3.
Natural coagulants: Instead of using chemical coagulants, use more environmentally friendly ones like Moringa oleifera seeds or chitosan, which come from the shells of crustaceans. These natural coagulants can help oil droplets and solids in suspension stick together, making it easier to separate them from the draw solution. The hydrophilicity of cellulose nanocrystal plays the most important and dominant role in the performance of all modified membranes [73]. To generate flat sheets with CH-O hydrogen bonds, cellulose chains are joined together by OH-O-type hydrogen bonds. These interactions involve nonbonding forces, including electrostatic, hydrogen bonding, and van der Waals forces. Here, cellulose nanocrystals interact strongly with water because of its hydrophilic nature. Nevertheless, the intermolecular hydrogen bond losses within the chains of cellulose are replaced by new hydrogen bonds created by water molecules during the water cellulose contact. The glycosidic linkages in the cellulose molecule are surrounded by substantial anti-bonding electron clouds. The approach of the water molecules induces a polarization in these anti-bonding electron cloud structures and an electrostatic dipole can be produced by distorting electron clouds. The concept of polarizability results in the development of a wave dipole. The interactions are dominated and defined by the characteristics of the hydrocarbon chains. The Pauli Principle's repulsion component prevents the chains from collapsing. There could be a variety of interactions, including attractive or repulsive interactions between water molecules and permanent dipoles found in cellulose polymers, induction interactions between permanent water molecule poles and induced multipoles found in cellulose chains, and any pairs of molecules resulting from interactions on instantaneous multi-poles [73]. The reason disused here is valid for all the TFN membranes but the contradiction between TFN-7 and TFN-5 membrane was generated when it comes to the salt and oil rejection efficiency, which is the main aim of the research; the lower salt and oil flux of TFN-5 membrane set a threshold point with respect to concentration of CNC.
According to the solution-diffusion theory, the FO solute flux is another essential FO parameter that is proportional to the concentration difference across the membranes. For realistic FO processes, membranes with minimal solute flux are preferred [54]. Comparing the solute flux through the CNC-nanoparticle-incorporated TFN membranes to the control

Conclusions
In the current study, thin-film nanocomposite membranes were developed by incorporating palm-tree-leaf-derived CNC to the PA layer of the TFC membrane. CNCs were developed from date palm leaves and different characterization studies confirmed the successful formations of CNCs and the effective incorporation of CNCs in the PA layer. From the TEM analysis, the size CNC was in the range of 78-100 nm. The results from the contact angle analysis showed that all membranes are hydrophilic, but the polyamide membrane incorporated with cellulose nanocrystals was more hydrophilic. From the FO experiments, it was confirmed that that the TFN-5 membrane showed better FO performance in PW treatment. Pristine TFC and TFN-5 membrane exhibited 96.2% and 99.0% salt rejection and 90.5% and 97.45% oil rejection. Further, TFC and TFN-5 demonstrated 0.46 and 1.61 LMHB pure water permeability and 0.41 and 1.42 LHM salt permeability, respectively. The reason for high flux, salt, and oil rejection of TFN-5 was primarily the uniform dispersion of CNC with the PA layer, which allows the water molecules to interact with the inductively activated cellulose nanocrystal molecules and form a dense water layer, as the water molecules. Therefore, the fabricated TFN-5 membrane could help in overcoming the present issues related to the TFC FO membranes used in produced water treatment process.