Facile synthesis of novel calcium silicate hydrated-nylon 6/66 nanocomposites by solution mixing method.

In this article a facile and green procedure for the synthesis of novel calcium silicate hydrated-nylon 6/66 nanocomposites is proposed. Calcium silicate hydrate (CSH) was synthesized by a hydrolysis technique assisted by ultrasound and using sodium dodecyl sulphate (SDS) as surfactant. CSH-nylon 6/66 nanocomposites were obtained by a solution mixing method at CSH loadings of 2.5, 25, 50 and 75 weight percent (samples CA, CD, CB and CC, respectively). The synthesis of CSH was confirmed by DRX and ATR-FTIR techniques; the CSH sample presents as mesoporous with a diameter between 3.34 nm and 52.68 nm and an average size of 27.07 nm; the specific surface area of the CSH sample was 343.99 m2 g-1. The formation of the CSH-nylon 6/66 nanocomposites was confirmed by ATR-FTIR, SEM, XRD, TGA, DSC and XPS techniques. The crystallization and melting temperatures (T m and T c, respectively) of CSH-nylon 6/66 nanocomposites occur at a slightly lower temperatures than those of neat Ny 6/66. These results suggest a slight decrease of the crystallite size and crystallization rate of nylon 6/66. The fusion enthalpy (ΔH f) decreases with increase in CSH content in nylon 6/66, which can be associated to a good dispersion. The XRD peaks of the nylon 6/66 at 19.99° and 23.77° were displaced at slightly higher values of 2θ with the incorporation of CSH in the polymer forming nanocomposite materials. This journal is © The Royal Society of Chemistry.

Introduction

The interest in calcium silicates has grown in different fields such as biomaterials and wastewater treatment due to the capability of recovering phosphates from aqueous environments. Some calcium silicates like wollastonite, olivine and β-CaSiO3, have been reported as bioactive materials because of their ability to form hydroxyapatite (Hap) over their surface, but between the different types of silicates, calcium silicate hydrate (CSH) is distinguished for the presence of –OH groups and Ca2+ ions that react with the PO43− groups providing a high bioactivity, and for that, it is considered a promising material for bone regeneration.[1-6] Besides the chemical composition of the CSH, characteristics such as specific surface area and porosity must also be considered to improve the bioactivity of the material, although there are some CSH with crystalline structures. The amorphous form of CSH can contribute to the obtaining of a porous morphology, and for that, it is necessary to find a synthesis method that allows the control of these properties.[1]

In addition to the characteristics mentioned above, the biomaterials should have good mechanical properties and be easily processed to make different pieces such as bone prosthesis or dental implants that are more durable and efficient than the ones made with conventional materials.[7-11] Ceramic materials are fragile and are not suitable for use in applications that require high load. In order to improve its mechanical properties, composite materials of ceramics with polymers like chitosan, polyamides and polycaprolactone have been studied as biomaterials.[7,9,12-14]

Among the polymers used in the field of biomaterials, the polyamides, also known as nylons, are an interesting group due to their chemical structure that allow a good interaction with ceramics like HAp, also, they have shown mechanical properties similar to human bones.[12] Some types of nylons that have been reported before for synthesize composite materials are nylon 12, nylon 6, and nylon 6,66 with layered silicates and organoclays.[12,15-18] Nylon 6/66 composites have been synthetized before with HAp as a filler, showing good bioactivity and good mechanical properties, for that it could be possible for composite materials made with CSH and nylon 6/66 show good bioactive behavior and good mechanical properties.

A common method to synthetize polymer matrix composites consist in the melting of the polymer and the subsequent incorporation of the ceramic in the melted polymer, needing high temperatures to melt the polymer and fabricate the composite. A more facile method to synthesize this type of composites is the solution mixing method that consist in the dissolution of the polymer in an accurate solvent where the ceramic particles are dispersed. This method ensures the homogeneity of the composite.[19]

In this study the synthesis of nanocomposite materials of CSH and nylon 6/66 through a facile method is investigated for first time, with the aim to obtain new nanocomposite materials with possible applications in bone regeneration, fabrication of prosthesis and in odontology.

Materials and methods

Materials

Calcium nitrate (Ca(NO3)2·4H2O, 99%), sodium meta-silicate (Na2SiO3, 44–47% SiO2), sodium lauryl sulfate (SDS, 99%), sodium hydroxide (NaOH, 99%), nylon 6/66 (M.W. 29 954 g mol−1), anhydrous ethanol and formic acid (95%) were purchased from Sigma-Aldrich.

Synthesis of CSH by hydrolysis and ion exchange

CSH was synthetized by a modification of the method reported by Mehrali et al.[20] A solution 0.2 M of Ca(NO3)2 was prepared and the pH value was adjusted to 9 with a solution 0.1 M of NaOH; after that, SDS was added in a concentration equal to its critical micellar concentration (CMC). Subsequently, a solution 0.2 M of Na2SiO3 was mixed with the solution of Ca(NO3)2 and the mixture was left under ultrasonic irradiation (SONICS, Ultrasonic Processor, 20% amplitude, 750 W) for 15 min at 85 °C. The obtained white product was washed with deionized water and ethanol to eliminate the surfactant and finally it was dried in an oven at 120 °C for 2 hours.

Synthesis of CSH-nylon 6/66 nanocomposite materials by solution mixing method

A previously established amount of nylon 6/66 pellets was dissolved in 6 ml of formic acid; after that, a suspension prepared with 0.2 g of the CSH into 15 ml of ethanol was added to the solution and the mixture was left under stirring for 15 min at 35 °C. Next, the temperature was raised to 45 °C and the stirring was turned off for 24 hours to evaporate the solvent. The white film obtained was then washed with deionized water and dried in an oven at 100 °C for 2 hours. Table 1 shows the synthesis conditions used to obtain four different composite materials and the synthesis procedure is schematized in Fig. 1.

Synthesis conditions used to obtain CSH-nylon 6/66 nanocomposites

Sample	Nylon 6/66 weight %	CSH weight %
CA	75	25
CD	50	50
CB	25	75
CC	2.5	97.5

Fig. 1

Synthesis procedure used for the obtention of CSH-nylon 6/66 nanocomposite materials.

Characterization

The FTIR spectra were obtained with a Thermo Scientific spectrometer in the ATR modality. A X-ray diffractometer Rigaku Ultima IV (Cu Kα, 10° min−1, 2 theta/theta, D-Tex, 40 KV, 44 mA) was used to characterize the calcium silicate sample and their composites with nylon 6/66. The nitrogen adsorption/desorption isotherm of calcium silicate sample was obtained using a Beckman Coulter SA3100 equipment. The morphology of the samples was investigated with an electronic microscope Philips XL 30 ESEM, equipped with an energy-dispersive X-ray (EDX) microanalysis system.

The thermal stability of CSH, nylon 6/66 and CSH-nylon 6/66 nanocomposites was determined using thermogravimetric analysis (TGA). Thermogravimetric measurements were performed using a PerkinElmer, TGA 4000 thermogravimetric analyser from 25 to 800 °C with a heating rate of 10 °C min−1 and nitrogen gas flow rate of 20 cm3 min−1. Differential scanning calorimetry (DSC) was employed to investigate the effect of CSH on the melting and crystallization behavior of nylon 6/66. Samples of neat nylon 6/66, CB and CD were studied using a TA Instruments DSC model Discovery 2500, using a heating and cooling rate of 10 °C min−1 between 30 and 300 °C under an inert nitrogen atmosphere. The samples were held at 300 °C for 5 min prior to cooling to remove previous thermal history. The samples were then cooled to 30 °C at 10 °C min−1 and reheated again to 300 °C at 10 °C min−1.

Chemical binding was analyzed by X-ray photoelectron spectroscopy (XPS) performed with a Thermo Scientific equipment, under high vacuum (9.5 × 10−9 mbar) operating with Al Kα radiation at 12 KV and 40 W; each sample was sputtered 15 seconds for a better analysis of the surface.

Results and discussion

Characterization of CSH

Fig. 2A shows the ATR-FTIR spectrum of the sample of calcium silicate. The band at 961 cm−1, can be attributed to a coupling of the vibrations of the Si–O–Si, Si–OH and Si(OSi)3O–Ca groups. The band at 3545 cm−1 is attributed to the stretching vibration of Si–OH⋯H2O, this band and the one at 1631 cm−1 indicate the presence of water in the chemical structure of calcium silicate. Absorption band at 1411 cm−1 corresponding to the binding vibration of the C–O indicates the presence of CO23− groups, this is because the sample adsorbs CO2, and due to its nature, it is not possible to avoid this phenomenon once it is exposed to the environment.[20-25] The diffraction pattern of the sample of calcium silicate is show in Fig. 2B; the presence of CSH (CaSiO3·H2O PDF #03-0606) was identified. Also, calcium carbonate is presented (CaCO3, PDF #05-0586); the formation of this phase maybe took place during the synthesis process, where CO2 from the atmosphere was absorbed due to the elevated pH conditions. The low-intensity diffraction peak at 2θ = 29.4° indicates low crystallinity of CSH.

Fig. 2

(A) ATR-FTIR spectrum and (B) XRD pattern of the calcium silicate hydrated (CSH).

Specific surface area was estimated according to Brunauer–Emmet–Teller (BET) method and the pore size distribution was calculated according to the Barret–Joyner–Halenda (BJH) model with the data of the nitrogen desorption isotherm. The nitrogen adsorption/desorption isotherm presented in Fig. 3A corresponds to a type IV isotherm according to the IUPAC classification, which is characteristic of a mesoporous solid. The pore size distribution indicates that the CSH sample presents porous with a diameter between 3.34 nm and 52.68 nm and an average size of 27.07 nm. The specific surface area obtained was 343.99 m2 g−1, this result can ensure a higher bioactivity due to the increase of sites for formation of Hap; also the presence of mesoporous is a suitable characteristic for biomaterials for bone regeneration because they allow the free movement of biomolecules like proteins and induce the adhesion of cells.[8,26-28] The SEM image shown in Fig. 3B suggests that the CSH consists of agglomerated nanoparticles and it has high porosity. Energy spectrum and element mapping images of Si, Ca and O of the CSH are shown in Fig. 3C. The value of the atomic ratio of Ca/Si is equal to 0.91, which is close to the expected theoretical value of 1; the difference between both values is due to EDX microanalysis is not a quantitative technique.

Fig. 3

(A) Adsorption–desorption isotherm and pore size distribution, (B) SEM micrograph at 75 000× (inserted micrograph was obtained at 1000×) and (C) Energy spectrum and element mapping images of Si, Ca and O of the CSH.

Characterization of CSH-nylon 6/66 nanocomposite materials

The ATR-FTIR spectrum of the CSH and ATR-spectra of the samples CA, CB, CC and CD are presented in Fig. 4A. It can be observed that the characteristic bands of the amide at 3293, 1631 and 1533 cm−1 (νN–H, νCO, νC–N and δN–H) are displaced to higher wave number as the amount of CSH increases (see Fig. 4B and C).

Fig. 4

(A) ATR-FTIR spectra of the samples CA, CB, CD, CC and Ny 6/66 from 4000 to 400 cm−1; (B) spectra from 3500 to 3000 cm−1 and (C) spectra from 1660 to 1500 cm−1.

The typical bands of the methylene groups at 2933 and 2859 cm−1, corresponding to the asymmetric and symmetric vibrations of C–H are also displaced to higher wave number. In the composite materials the band at 961 cm−1 is not present, but the appearance of the typical bands of the Si–O–Si are clearly presented from 1066 to 1047 cm−1 and 794 to 792 cm−1. Therefore, it can be inferred that the interaction between nylon 6/66 and CSH occurs trough amide groups of nylon 6/66 with Si–OH groups of the CSH. Table 2 shows the characteristic vibration frequencies in ATR-FTIR spectra of the samples CA, CB, CC and CD and the assignments according to the literature.[16,20-23,29-32]

Characteristic vibration frequencies (cm−1) in FTIR-ATR spectra of the synthetized samples[16,20–23,29–32]

Assignments	Samples synthetized in this work						Literature
	CA	CD	CB	CC	Ny 6/66	CSH
N–H stretching	3299	3300	—	—	3293	—	3296–3335
N–H overtone of amide II	3077	—	—	—	3079	—	3070–3082
CH methylene asymmetric stretching	2933	2934	—	—	2933	—	2920–2934
CH methylene symmetric stretching	2859	2862	—	—	2859	—	2851–2860
CO stretching amide I	1633	1633	1633	1633	1631	—	1632–1660
C–N stretching and N–H bending amide II	1534	1537	1538	—	1533	—	1530–1537
CH2 scissoring	1464	1463	—	—	1465	—	1466
CH2 wagging	1367	1363	—	—	1371	—	1370–1373
Amide III	1274	—	—	—	1270	—	1262–1279
Si–OH⋯H2O	—	—	3500–3100	3500–3100	—	3545	2800–3700
H2O molecular	—	—	—	—	—	1631	1600–1650
CO32− asymmetric stretching	—	—	—	—	—	1411	1410–1510
Si–O–Si stretching	1066	1060	1050	1047	—	—	1095–900
Si(OSi)3O–Ca	935	936	941	943	—	961	890–965
Si–O–Si stretching or bending	792	793	794	794	—	—	760–850
C–O	—	—	—	—	—	875	856–880

In the thermogravimetric curves (Fig. 5) a main weight loss can be seen between 350 °C and 550 °C for the nylon 6/66 and the samples CA, CB, CC and CD, this is due to the decomposition of the polymer chains. The starting degradation temperature of the pristine nylon 6/66 take place at 350 °C, this temperature value decreases for the samples CA, CB, CC and CD, having the lower degradation temperature for CB sample at 333 °C and the higher initial degradation temperature for CC sample at 348 °C. However, the final degradation temperature of the nylon 6/66 at 445 °C, increases as the amount of CSH in the polymer matrix increases too, obtaining the higher final degradation temperature in sample CC at 527 °C. This indicates that the samples CA, CB, CC and CD are thermally stable in a longer range of temperature, which can be due to the formation of bonds between the nylon 6/66 and the CSH. A second weight loss is seen in the TG curve of nylon 6/66; this loss starts at 603 °C and in this case the initial degradation temperature increases as the amount of CSH increases too, obtaining the higher initial degradation temperature in the composite CC at 613 °C. All samples of CSH-nylon 6/66 present higher thermal stability than pristine nylon 6/66. For the CSH a total weight loss of 30% occurs mainly due to the evaporation of adsorbed water and water bonded to the crystalline structure. After the degradation of the polymer matrix, some changes still occur in the composite materials such as the change of phase from CSH to wollastonite type silicate.[33-36]

Fig. 5

TG curves of the samples CA, CB, CC and CD and TG curves of nylon 6/66 (Ny 6/66) and the CSH.

The DSC curves of neat nylon 6/66 and of the samples CB and CD during the first cooling and second heating processes are shown in Fig. 6A and B, respectively. Table 3 summarizes the data from the DSC curves. The crystallization temperature (Tc) of the samples CB and CD occurs at a slightly lower temperature than that of neat Ny 6/66. The high quantity of CSH added could deaccelerate the Ny 6/66 nucleation rate and consequently lead to the decrease of the crystallization rate, and as a result, the Tc during the cooling decreased. Also, the addition of CSH had a slight impact on the melting temperature (Tm); this may be is related to a slight reduction in crystallite size with the presence of CSH in the nanocomposites and consequently lead to the lower Tm value. However, an obvious decrease in the fusion enthalpy (ΔHf) was observed, due to the addition of CSH. This observation is in according to Venkataramani et al., (2009); they study the structure and properties of nylon 6/66 with a molecular weight of 35 721.92 g mol−1 and a nylon 6/66 organoclay composite (2%). The fusion enthalpy (ΔHf) and melting temperature decrease with increase in clay content in nylon 6/66.[17] Liu et al. (2018) investigated on crystallization of nylon 6/66 nanocomposites with exfoliated organoclay into the range of 1 to 5 weight percent, which was introduced and melt-blended with PA6/66 (Mn = 17 000 g mol−1); they reported that Tc during the cooling increases.[18]

Fig. 6

DSC curves of the nylon 6/66 and CSH-nylon 6/66 nanocomposites during the first cooling (A) and second heating (B) scans.

DSC data of the Ny 6/66 and the CSH-nylon 6/66 nanocomposites. The crystallization temperature (Tc) was recorded from the first cooling scan; the melting point (Tm) and fusion enthalpy (ΔHf) were recorded from the second heating scan

Sample	T c (°C)	T m (°C)	ΔHf (J g−1)
Ny 6/66	211.44	243.80	76.086
CD	209.76	243.09	57.207
CB	209.03	240.87	37.212
Ny 6/66 (ref. 17)	118.7	193.5	32.8
Ny 6/66 (ref. 18)	157	194	47.8

The Fig. 7 shows the XRD patterns of the samples CA, CB, CC and CD; XRD patterns of nylon 6/66 and CSH are also included. It is seen that the XRD pattern for nylon 6/66 shows its crystalline nature with the characteristic peaks at 2θ = 19.99° and 23.77° which belong to the monoclinic form; similar results have been reported for PA6/66 and its nanocomposites with different organoclay content.[17] It is noticed that the two peaks of the nylon 6/66 are slightly shifted towards higher 2θ values with the incorporation of CSH in the composition of the samples CA, CB, CD and CC (see Table 4). This suggests that CSH was incorporated to nylon 6/66 forming composite materials. XRD pattern of sample CC also shows two small diffraction peaks at 26° and 30° that correspond to the presence of calcium formate, a subproduct from the reaction between CaCO3 present in the CSH sample and the formic acid used to dissolve the nylon 6/66. Calcium formate is soluble in water at 25 °C, therefore, it is possible to eliminate it easily.

Fig. 7

XRD patterns of the samples of CA, CB, CC and CD and XRD patterns of the precursors.

2θ values of the Ny 6/66 and the CSH-nylon 6/66 nanocomposites (CA, CD, CB and CC)

Sample	2θ degrees
	Peak 1	Peak 2
Ny 6/66	19.99	23.77
CA	20.42	24.30
CD	20.64	24.62
CB	20.34	24.06
CC	20.36	24.14

The morphology of the samples CA, CB, CC and CD was investigated by scanning electron microscopy (SEM). The Fig. 8 show the micrograph of the samples CA, CD, CB and CC. Also, energy spectra and element mapping images of Si and C of these samples are shown in this figure. It is observed that the samples CA and CD consist of a polymer matrix that is filled with very few agglomerates of CSH. The samples CB and CC consists of a ceramic matrix with a high amount of CSH particles. The morphology of the sample CD is very different to the other and it has more porous; this sample was possibly exposed to a longer analysis time by SEM and the energy of the beam could have burned it, leaving pores. The energy peaks corresponding to Si, Ca, C and O are observed in the energy spectra of the samples CA, CD, CB and CC. A semiquantitative analysis of the atomic ratio of Si : C for the samples CA, CD, CB and CC was performed and values of 0.045, 0.119, 0.648 and 1.007, respectively, were obtained. These measured values are lower than the expected theoretical values of 0.097, 0.194, 0.972 and 7.775 for the samples CA, CD, CB and CC, respectively, because EDX microanalysis is not a quantitative technique. The element mapping images of Si and C of the samples CA, CD, CB and CC suggest that they are homogeneous in their chemical composition.

Fig. 8

SEM micrographs, energy spectra and element mapping images of Si and C of the samples CA, CB, CC and CD.

To investigate the chemical environment in the surface of the samples CA, CB, CC and CD, one XPS analysis was performed; the results are shown in Fig. 9. In the XPS binding energy spectra of the samples CA, CB, CC and CD the appearance of the peaks of Si 2p and the increasing of the intensity of the peak of O 1s can be seen; the displacement of the O 1s and the C 1s peaks shows the changing on the chemical environment in the surface of the samples (Fig. 9A). The deconvolution of the peak C 1s for the samples CA, CB, CC and CD is presented in Fig. 9B–F. The peak of the C 1s on the pristine nylon 6/66 was deconvoluted into three signals indicating the presence of CO, C–N and C–C bonds (Fig. 9B). The signal of C–O bonding appears with the addition of the CSH to the polymer (samples CA, CB, CC and CD), which indicates the formation of new bonds between the carbon atoms of the polymer chain and the groups –OH of the CSH (Fig. 9C–F). The O 1s peak of spectra of pristine nylon 6/66 and the CSH and the O 1s peak of spectra of the samples CA, CB, CC and CD was also deconvoluted (Fig. 10). It is observed that there are two oxygen environments in the spectra of pristine nylon 6/66 that corresponding to N–CO and CO bonds. XPS spectra of the samples CA, CB, CC and CD have three other signals that corresponding to Si–O–Ca, Si–O–Si and Si–OH bonds from the CSH. The intensity of the signal of Si–O–Ca decreases as the amount of nylon 6/66 increases. Intensity of the signal of Si–OH of the CSH decreases as well as the intensity of the signal Si–O–Ca of the samples CA, CB, CC and CD.

Fig. 9

(A) General XPS binding energy spectra of the samples CA, CB, CC and CD and XPS spectra of pristine nylon 6/66 and the CSH; and deconvolution of carbon 1s peak of (B) nylon 6/66, (C) composite CA, (D) composite CD, (E) composite CB and (F) composite CC.

Fig. 10

Deconvolution of O 1s peak of (A) pristine nylon 6/66, (B) composite CA, (C) composite CD, (D) composite CB, (E) composite CC and (F) CSH.

Based on the results of the ATR-FTIR spectra, XRD and XPS analysis of the spectra of the samples CA, CB, CC y CD, a structure of CSH-nylon 6/66 nanocomposites is proposed in Fig. 11.

Fig. 11

Representation of the bonds between the CSH and nylon 6/66 in the composite materials.

Conclusions

According to the ATR-FTIR spectra, XRD patterns and the XPS analysis, it can be assumed that the solution mixing method, using formic acid to dissolve the nylon 6/66, allowed to easily synthetize CSH-nylon 6/66 nanocomposites. The synthesis of CSH-nylon 6/66 nanocomposites took place by the interaction between calcium atoms from the CSH with oxygen atoms from the nylon, as well as by the interactions between groups Si–OH from the CSH with groups –NH from the polymer chain. The incorporation of the CSH to nylon 6/66 increases its thermal stability. The crystallization and melting temperatures (Tm and Tc, respectively) of CSH-nylon 6/66 nanocomposites occurs at a slightly lower temperature than that of neat Ny 6/66. These results suggest a slight decrease of the crystallite size and crystallization rate of nylon 6/66. Due to the high value of specific surface area of the CSH (343.99 m2 g−1) and the chemical structure of CSH-nylon 6/66 nanocomposites, they can be used in the fabrication of bone prosthesis and odontology implants.

Conflicts of interest

There are no conflicts to declare.