Preparation of polybutylene terephthalate/artificial marble wastes composites with simultaneously enhanced thermal,crystallization,and impact properties by in situ polymerization

Abstract

The treatment of artificial marble wastes (AMWs) is a difficult aspect of the artificial marble industry and has enormous impacts on the environment. Herein, a series of polybutylene terephthalate (PBT)/AMWs composites were prepared by in situ polymerization. The effects of AMWs content (1–10 wt%) on the thermal stability, crystallization rate, and impact strength of the PBT/AMWs composites were investigated in detail. The results showed that the composites containing 10 wt% of AMWs exhibited the best performance. Due to the high thermal resistance and uniform distribution of the AMWs particles, the heat deflection temperature reached 67.40°C with optimal thermal stability. Additionally, under heterogeneous nucleation, the crystallization rate was also the highest, and impact strength reached 17.29 kJ/m² due to the partial core-shell structure and hardened matrix effects of the AMWs particles.

Keywords

Polybutylene terephthalate artificial marble wastes composites in situ polymerization partial core-shell structure

Introduction

The marble industry has developed rapidly in recent years due to the continuous development of mining resources. However, during marble mining and processing, as much as 60% of the total product generated is solid waste material, including waste, waste powder, and waste mud.^1-3 These solid waste materials occupy large volumes in landfills, causing serious environmental pollution and threats to public health.^4-7 Artificial marble wastes (AMWs), which are by-products of artificial marble sawing or polishing, are one of the most common types.⁸ Thus, converting AMWs into valuable resources remains a significant but imperative challenge.

Over the past few years, considerable research has been conducted on the recycling of AMWs. Ahmed et al.⁹ prepared a hybrid composite material consisting of marble waste, shell ash, and natural rubber, and the results showed improved mechanical properties such as flexural strength, compression strength, hardness, and wear resistance. Kar et al.¹⁰ studied how the addition of marble waste materials into polyethylene terephthalate (PET) composites improved the hardness, bending strength, and conductivity of the composites. Meanwhile, Lu et al.¹¹ produced high-strength ceramic containers through surface modification and low-temperature sintering of the AMWs. Awad et al.¹² and Pappu et al.¹³ prepared a novel composite material by mixing marble dust particles with low density polyethylene, and the flexural strength and thermal stability of the composite material were effectively improved. In addition, Nayak et al.¹⁴ added AMWs as secondary fillers to a glass-resin composite system, which effectively reduced the wear rate of the composite material while also reducing cost. Zhang et al.¹⁵ prepared polyvinyl alcohol (PVA)/AMWs composites via melt processing. The results showed that the melt-processing window of 76.9°C for PVA significantly increased when combined with 10 wt% of AMWs, which was due to the interfacial hydrogen bonding interactions between the AMWs and the PVA molecules.

Polybutylene terephthalate (PBT) is an important thermoplastic resin that is widely used in applications such as automobile and mechanical parts manufacturing due to its excellent mechanical properties, corrosion resistance, and dimensional stability.^16-19 However, neat PBT has disadvantages such as low heat deflection temperature and weak impact strength, which limit its applications.^20-22 Therefore, it is commonly combined with reinforcing materials to meet the requirements for high-performance materials.^23-28

In this work, PBT/AMWs composite materials were successfully prepared by in situ polymerization, and the effects of AMWs content on the thermal stability, crystallization rate, and impact strength of the PBT/AMWs composites were investigated. The purpose of this study was to utilize the AMWs as a resource and provide a new perspective for the applications of PBT composites in order to efficiently recover AMWs for economic and environmental benefits.

Experimental

Materials

AMWs were collected from Guangxi Lisheng Stone Industry Co., Ltd, Hezhou, China. Dimethyl terephthalate (DMT) (Aladdin, 99% purity) and 1,4-butanediol (BDO) (Aladdin, 98% purity) were used to synthesize PBT. Tetrabutyl titanate (Aladdin, ≥99% purity) was used as the catalyst for trans-esterification.

Material preparation

The AMWs used in this study were treated using 1000 mesh wet sieving and then dried at 80°C for 10 h. The trans-esterification of DMT (97.09 g, 0.5 mol) with BDO (99.13 g, 1.1 mol) was carried out in the presence of tetrabutyl titanate as the catalyst in a 250 mL three-neck flask. The system was equipped with a mechanical stirrer, a vacuum pump, and a condensing device. The DMT, BDO, and catalyst mixture were continuously stirred throughout the reaction at 190°C. When the methanol evaporation rate reached 93% of the theoretical value, 1 wt% (1.21 g) of AMWs was added to the reaction and stirred continuously for 10 min. Then, to start polycondensation, the mixture was vacuumed at 250°C, and a composite containing 1 wt% of AMWs was obtained. Neat PBT was synthesized using the same steps as previously stated but without the addition of AMWs. According to the weight percentage of AMWs, the composites were denoted by PBT-0 (0 wt% of AMWs), PBT-1 (1 wt% of AMWs), PBT-3 (3 wt% of AMWs), PBT-5 (5 wt% of AMWs), PBT-7 (7 wt% of AMWs), and PBT-10 (10 wt% of AMWs). Afterward, the composites were crushed and melted into three-dimensional strip samples (80 mm × 10 mm × 4 mm), using an SZS-20 micro-injection machine (Wuhan Ruiming Experimental Instrument Co., Ltd, Wuhan, China) at a melting temperature of 260°C, a mold temperature of 60°C, and a holding time of 40 s.

Characterizations

Particle size analysis

The particle size analysis of the AMWs was conducted using a BT-2600 laser particle size analyzer (Dandong Baite Instrument Co., Ltd, Dandong, China), with water as the dispersant. The shading index was set to 10%–15%, and the rotation speed was 1600 r/min.

Gel permeation chromatography measurements

The molecular weights and polydispersity indices of the PBT/AMWs composites were tested at 35°C by gel permeation chromatography (GPC) using a Waters GPC device (Agilent, USA) equipped with a Watersmodel 1515 autosampler, a 2414 refractive index detector, and an Agilent PLgel 5-μm MIXED-C chromatographic column (made in GB). Hexafluoroisopropanol was used as the eluent, and the flow rate was 1 mL·min⁻¹. Additionally, polymethyl methacrylate (PMMA) was employed as the standard.

Wide-angle X-ray diffraction (XRD) measurements

X-ray diffraction (XRD) measurements were performed on an Ultima IV instrument (Rigaku, Japan), using Cu-Kα radiation (operated at 40 kV and 40 mA) between 5° and 80° at 10°/min.

Thermal gravimetric analysis

Thermal gravimetric analysis (TGA) measurements were obtained using a TGA4000 instrument (PerkinElmer, USA). Each sample was approximately 9–10 mg, and the analysis was carried out in a nitrogen atmosphere, ranging from 30°C to 850°C, and with a heating rate of 10°C/min.

Heat deflection temperature tests

Heat deflection temperature (HDT) tests were conducted using an HDT/V-1103 instrument (Chengde Jinjian Testing Instrument Co., Ltd, Chengde, China) according to the GB/T 1634–2004 standard, and each sample was injected with a micro-injection machine and tested a minimum of five times.

Differential scanning calorimetry analysis

Differential scanning calorimetry (DSC) analysis was carried out on a DSC25 instrument (TA, USA). The non-isothermal crystallization and isothermal crystallization measurements were conducted in a nitrogen atmosphere; each sample was approximately 9–10 mg and sealed in an aluminum pan. Each sample was first heated from 30°C to 260°C at a heating rate of 20°C/min and was held at this temperature for 2 min to eliminate the effect of the thermal and processing history. For non-isothermal crystallization, each sample was cooled down from 260°C to 0°C for six cycles at various cooling rates of 1.25°C/min, 2.5°C/min, 5°C/min, 10°C/min, 20°C/min, and 40°C/min, respectively. After each cooling, heating to 260°C at 10°C/min was performed. For isothermal crystallization, each sample was rapidly cooled from 260°C to different crystallization temperature of 204°C, 206°C, 208°C, 210°C, 212°C, and 214°C, respectively. And then, each sample was kept at the corresponding temperature until the crystallization finished. Finally, heating to 260°C at 5°C/min was carried out.

Impact strength tests

The impact strength tests were performed using a CEAST 9050 impact testing machine (INSTRON, USA) according to the ISO 180 standard with unnotched samples. Each sample was tested a minimum of five times.

Flexural strength tests

The flexural strength tests were conducted employing an INSTRON 3367 universal material testing machine (INSTRON, USA) according to the ISO 178: 2001 standard. Each sample was tested a minimum of five times.

Tensile strength tests

The tensile strength tests were executed using an INSTRON 3367 universal material testing machine (INSTRON, USA) according to the ISO 527-1: 1993 standard. Each sample was tested a minimum of five times.

Scanning electron microscopy (SEM)

The surface morphology of the AMWs powder was observed using a scanning electron microscope (SEM) (S4800, Hitachi, Japan) operated at an accelerating voltage of 5 kV. Surface morphologies of the PBT/AMWs composites were also observed using an SEM (JSM-7610F, JEOL, Japan) operated at an accelerating voltage of 1.6 kV. The AMWs powder and composite sample surfaces were sputter coated with a light layer of gold.

Results and discussion

Surface characteristics of AMWs

Figure 1(a) shows the size distributions of the AMWs particles. The average particle size was 5.358 μm with a narrow particle distribution. The SEM image of the AMWs powder is shown in Figure 1(b)b, indicating that AMWs have the advantages of tiny particle sizing and appropriate specific surface areas, both of which are beneficial for the dispersion of AMWs in the PBT matrix.¹⁵ The TGA curves for the AMWs and neat CaCO3 are shown in Figure 1(c), clearly showing there are three steps in the TGA curve for the AMWs between 220°C and 600°C compared with neat CaCO3. This can be interpreted as the unsaturated resin coating on the surface of AMWs, which occurred due to decomposition.

Figure 1.

(a) Particle size distribution and (b) SEM image of the AMWs powder. (c) TGA curves for the AMWs and neat CaCO3.

Gel permeation chromatography measurements

The molecular weights (Mn and Mw) and polydispersity indices (PDI) of the PBT/AMWs composites were measured by GPC, and the main parameters obtained from the GPC curves are presented in Table 1. All of the PBT/AMWs composites maintained high molecular weights, and PDI values were concentrated in the range of 2.29–2.58. The characteristic peaks in the outflow curves of the composites with different AMWs contents slightly fluctuated, as shown in Figure 2. Thus, it was concluded that the AMWs did not affect PBT polymerization.

Table 1.

The main parameters obtained from GPC measurements.

Samples	Mn (×10⁴ g/mol)	Mw (×10⁴ g/mol)	PDI
PBT-0	1.964	4.827	2.457
PBT-1	1.442	3.570	2.476
PBT-3	1.590	3.653	2.297
PBT-5	1.591	3.682	2.313
PBT-7	1.609	4.146	2.576
PBT-10	1.605	4.118	2.564

Figure 2.

GPC outflow curves of the PBT/AMWs composites.

XRD analysis

XRD was carried out to assess the crystalline structure and crystallite sizes of the PBT/AMWs composites. Crystalline Bragg peaks were evident for all the XRD patterns, as shown in Figure 3(a). The new peaks for the composites were similar to the expected AMWs characteristic peaks, indicating that the composition did not change.

Figure 3.

(a) XRD patterns of the AMWs and PBT/AMWs composites. (b) Crystallite sizes of the PBT/AMWs For Peer Review composites.

The effects of adding AMWs on crystallite size were quantitatively evaluated through the Debye—Scherrer equation,²⁹ as follows

L_{h k l} = \frac{k λ}{β \cos θ}

(1)

where L_hkl represents the average size of the microcrystals perpendicular to

(h k l)

crystal plane (nm), k is the dimensionless shape factor constant with a value of 0.94, and λ, β, and θ denote the X-ray (nm) wavelength, the fullwidth at half maximum (FWHM), which corresponds to the scattering in radians, and the Bragg angle for peak diffraction, respectively. Five characteristic peaks were used for FWHM calculation, which were observed at the 2θ of 17.3°, 23.4°, 25.2°, 29.4°, and 30.9°. As shown in Figure 3(b), the crystallite sizes in the PBT/AMWs composites gradually decreased from 19.69 to 17.95 nm. This result may be due to the nucleation effect of the AMWs particles, which affected the inhomogeneous nucleation of the PBT matrix. Nucleation occurred more easily at the interface of the two substances, compared with homogeneous nucleation, due to the lower activation energy of heterogeneous nucleation.³⁰ Therefore, numerous nucleation sites were available due to the presence of the AMWs, which promoted the heterogeneous nucleation of PBT, resulting in an increase in nucleation density and thereby reducing the crystallite sizes.

Thermal stability analysis

The TGA curves, Derivative Thermogravimetry (DTG) curves, and heat deflection temperature (T_hdt) for the PBT/AMWs composites are shown in Figure 4, and the thermal parameters are listed in Table 2. The T_5wt% and T_max represent the initial decomposition temperature and maximum weight loss temperature, respectively. Both exhibited an overall upward trend as the AMWs content increased, which indicated that AMWs were conducive to improving thermal stability.^31,32 This may have been due to the high thermal resistance of the AMWs and the strong interactions between the PBT matrix and AMWs filler, resulting in the restricted movement of the polymer chain.³³ In addition, the addition of AMWs can also promote the entanglement of polymer molecular chains. Therefore, as the AMWs content increased, the higher the energy required for molecular chain fracture, the higher the corresponding temperature.³⁴ Furthermore, the heat deflection temperature of the composites increased from 48.72°C to 67.40°C, which may have been due to the uniform distribution of AMWs particles in the matrix.³⁵

Figure 4.

(a) TGA curves, (b) DTG curves, and (c) heat deflection temperature for the PBT/AMWs composites.

Table 2.

The thermal parameters obtained from TGA curves, DSC curves and heat deflection temperature of the PBT/AMWs composites.

Samples	T_5wt% (°C)	T_max (°C)	T_hdt (°C)
PBT-0	378.57	407.52	48.72
PBT-1	378.78	406.06	50.14
PBT-3	379.63	407.94	51.82
PBT-5	380.30	411.12	59.74
PBT-7	381.74	411.35	64.96
PBT-10	382.64	415.05	67.40

Crystallization behavior analysis

Figure 5 shows the changes in the crystallization curves as the AMWs content increased at different cooling rates. It was apparent that the crystallization onset temperature Tonset c and the crystallization peak temperature Tpeak c increased with the addition of AMWs when the cooling rate was maintained, which may have been due to the heterogeneous nucleation of the AMWs particles in the PBT matrix.^36–38 In addition, when the AMWs content was constant, the crystallization curves moved to the low-temperature region when the cooling rate increased. This was attributed to the molecular chains not having enough time to arrange into a crystalline phase during rapid cooling,³⁹ thus chain segment activity was poor and the crystallization was delayed, which lowered the crystallization temperature.

Figure 5.

Non-isothermal DSC curves for the PBT/AMWs composites at cooling rates of (a) 1.25°C/min, (b) 2.5°C/min, (c) 5°C/min, (d) 10°C/min, (e) 20°C/min, and (f) 40°C/min, respectively.

Figure 6 shows the comparative differences in crystallization peak temperatures for the PBT/AMWs composites with different content. At a cooling rate of 1.25°C/min, when only 1 wt% of AMWs was added, the Tpeak c increased by about 10°C compared with neat PBT and continued to increase with increased AMWs content. Similar results were obtained for other cooling rates, and the faster the cooling rate, the more significant the difference. The reason for this phenomenon was due to the addition of the AMWs material, which gradually improved the heterogeneous nucleation of PBT.

Figure 6.

Crystallization peak temperature Tpeak c of the PBT/AMWs composites at different cooling rates.

To investigate the isothermal crystallization behavior of the PBT/AMWs composites, crystallization kinetics were assessed, which are quantified by relative crystallinity X_t as a function of time t at different temperatures and obtained by

X_{t} = \frac{\int_{T_{0}}^{T} (\frac{d H_{c}}{d T}) d T}{\int_{T_{0}}^{T_{\infty}} (\frac{d H_{c}}{d T}) d T}

(2)

where T, T₀, T_∞, and (dH_c/dT) represent an arbitrary temperature, the crystallization onset, the end temperature, and the heat flow rate, respectively. The horizontal crystallization temperature scale can be transformed into a time axis, according to the following equation

t = \frac{T_{0} - T}{Φ}

(3)

where T₀, T, and Φ denote the temperature at which crystallization starts (t = 0), the temperature at time t, and the cooling rate, respectively.

As shown in Figure 7, as the temperature increased, the neat PBT required more time for crystallization, indicating that the crystallization rate decreased gradually. This was attributed to the fact that the crystallization rate was controlled by the nucleation rate at a high temperature, and under this condition, polymer chain mobility improved and the crystalline nucleus was unstable.⁴⁰ Thus, as shown in Figure 7(b)–(f), the crystallization rate of the PBT/AMWs composites increased gradually compared with neat PBT. This phenomenon was more apparent at higher temperatures, suggesting that sufficient nucleation sites were made available by the AMWs, which accelerated the crystallization process.

Figure 7.

Relative crystallinity Xt as a function of time t for the PBT/AMWs composites with the AMWs content of (a) 0, (b) 1 wt%, (c) 3 wt%, (d) 5 wt%, (e) 7 wt%, and (f) 10 wt%, respectively.

The Avrami model describes the relationship between relative crystallinity and crystallization time, and can be used to analyze the isothermal crystallization kinetics of most semicrystalline polymers and is expressed^41,42 as follows

1 - X_{t} = e x p (- k t^{n})

(4)

where X_t denotes the relative crystallinity at t, n represents the Avrami index, which contains information about the nucleation type and growth process, and k represents the crystallization rate constant, which is related to the nucleation and growth rate. Figure 8 shows the Avrami plots for the PBT/AMWs composites and the isothermal crystallization kinetic parameters obtained from these plots are listed in Table 3. These plots indicated a good linear relationship in the primary and middle crystallization stages, but some deviations appear in the later crystallization stage, which may have been due to secondary crystallization. From the slope and intercept of the linear plots, the Avrami index n and crystallization rate constant k values were obtained separately. Generally, the n value represents the number of growth points during the crystallization of polymer melt. It can be found from Table 3 that the n value increased with the addition of AMWs, which was related to the increase of microcrystalline nuclei. Therefore, AMWs can be considered as nucleating agents in the crystallization process of PBT, which increased the number of crystallization nucleation.

Figure 8.

Avrami plots of log [-ln(1-Xt)] versus log t for the PBT/AMWs composites with the AMWs content of (a) 0, (b) 1%, (c) 3%, (d) 5%, (e) 7%, and (f) 10%, respectively.

Table 3.

The isothermal crystallization kinetic parameters obtained from the Avrami plots of the PBT/AMWs composites.

Samples	T_c (°C)	n	k (min⁻¹)	t_1/2 (min)
PBT-0	204	2.51	1.80E-03	10.70
	206	2.37	4.00E-04	23.32
	208	2.36	2.00E-04	31.54
	210	2.21	1.61E-04	43.89
	212	1.95	3.10E-05	171.87
	214	1.99	1.32E-05	237.27
PBT-1	204	2.75	0.079	2.21
	206	2.76	0.012	4.33
	208	2.76	5.82E-03	5.66
	210	2.89	6.56E-04	11.16
	212	2.86	1.70E-04	18.36
	214	2.56	3.86E-05	45.89
PBT-3	204	2.73	0.318	1.33
	206	2.78	0.068	2.31
	208	2.60	0.016	4.28
	210	2.81	2.85E-03	7.08
	212	2.69	3.90E-04	16.08
	214	2.70	5.09E-05	33.86
PBT-5	204	2.72	0.324	1.32
	206	2.71	0.092	2.11
	208	2.51	0.025	3.77
	210	2.85	3.16E-03	6.65
	212	2.90	3.79E-04	13.32
	214	2.92	3.32E-05	30.29
PBT-7	204	2.61	0.780	0.96
	206	2.83	0.217	1.51
	208	3.01	0.035	2.70
	210	2.93	8.83E-03	4.43
	212	2.90	1.37E-03	8.56
	214	2.65	2.39E-04	20.24
PBT-10	204	2.64	1.408	0.76
	206	2.67	0.363	1.27
	208	2.70	0.061	2.46
	210	2.76	0.016	3.92
	212	3.02	1.39E-03	7.81
	214	2.88	1.96E-04	17.01

To more thoroughly study the effects of AMWs content on crystallization rate during the isothermal crystallization process, an important parameter t_1/2 was considered, which can be estimated⁴³ as follows

t_{1 / 2} = {(\frac{\ln 2}{k})}^{1 / n}

(5)

where t_1/2 is defined as the time required for a sample to reach half of the final crystallinity.⁴⁴

As shown in Figure 9, with an increase in crystallization temperature T_c, the t_1/2 value for the PBT/AMWs composites increased significantly, and the corresponding crystallization rate decreased. This indicated that the isothermal crystallization of the PBT/AMWs composites was controlled by nucleation. Therefore, it was evident that the crystallization time decreased rapidly at different crystallization temperatures after the AMWs were added, which agreed with the phenomenon observed in Figure 7.

Figure 9.

t_1/2 of the PBT/AMWs composites at different crystallization temperatures.

Mechanical properties analysis

After composite preparation, the samples were crushed and fabricated into a specific size (80 mm × 10 mm × 4 mm) using a micro-injection machine for impact strength tests, as shown in Figure 10(a)–(c). By gradually adding the AMWs, the impact strength of PBT significantly improved from 5.79 to 17.29 kJ/m², as shown in Figure 10(d). This was attributed to the AMWs particles, which had a partial core-shell structure during the formation process, as shown in Figure 11. The AMWs used in this experiment were treated through 1000 mesh wet sieving, the particle size was far smaller than the initial heavy calcium powder, which used in the synthesis of artificial marble, suggesting that the initial heavy calcium powder was cut open again in the cutting process, and the new section produced was not covered by unsaturated polyesters. This structure produced a toughening effect,^45–47 which absorbed the impact energy and hindered the further propagation of microcracks. In addition, the hardness of the AMWs particles was higher than that of the PBT matrix, and the hardened matrix effect may have also contributed to the improvement in impact strength.⁴⁸

Figure 10.

(a) Injection molding simulation diagram, (b) actual diagram, and (c) impact simulation diagram of a PBT/AMWs composite sample. (d) impact strength of the PBT/AMWs composites.

Figure 11.

(a) Formation of artificial marble and AMWs. (b) microstructure model of AMWs with partial core-shell structure.

As shown in Figure 12, the flexural strength and tensile strength of PBT/AMWs composites were also investigated in this work. The flexural strength and tensile strength increased with the increase of AMWs content, and reached the maximum at 3 wt%. It was due to that the AMWs filled PBT composites had higher stiffness and hampered the free mobility of PBT chains.49 This was also related to the appropriate dispersion of AMWs in PBT matrix and the proper stress transfer between the PBT matrix and AMWs.50 When the AMWs content exceeded 3 wt%, the decrease of flexural strength and tensile strength may be caused by the increment in stress concentration.

Figure 12.

The flexural strength and tensile strength of PBT/AMWs composites.

SEM analysis

SEM results indicated many fluvial-like steps on the impact fracture surface, which were not on the same plane when AMWs content increased, indicating enhanced interface interactions (Figure 13(a)–(f)). Starting with an AMWs content of 5 wt%, a wire drawing phenomenon appeared at marks ①, ②, and ③. Afterward, marks ③ and ④ become locally enlarged (Figure 13 (g) and (h)), and the wire drawing effect was evident and the distribution of the AMWs particles was uniform. This also indirectly indicated that the AMWs with partial core-shell structures toughened the PBT matrix and improved the impact strength. As a result, this agrees well with the impact strength test results.

Figure 13.

SEM images of impact fracture surface of the PBT/AMWs composites with the AMWs content of (a) 0, (b) 1 wt%, (c) 3 wt%, (d) 5 wt%, (e) 7 wt%, and (f) 10 wt%, respectively. (g) and (h) locally enlarged images of two places in graph (e) and (f), respectively.

Conclusion

In this study, PBT/AMWs composites were prepared by in situ polymerization, and the addition of AMWs into PBT enhanced the properties of the composite material, that is, thermal stability, crystallization rate, and impact strength. The results were attributed to two main reasons. Firstly, the AMWs particles possessed partial core-shell structures and were distributed uniformly throughout the matrix. Secondly, heterogeneous nucleation occurred at the interface between the AMWs particles and PBT. It is, thus, likely that the development of PBT/AMWs composites will provide opportunities for expanded PBT applications and the effective recycling of AMWs into high-value and high-performance composites.

Footnotes

Declaration of conflicting interests

The author(s) declared no potential conflicts of interest with respect to the research, authorship, and/or publication of this article.

Funding

The author(s) disclosed receipt of the following financial support for the research, authorship, and/or publication of this article: This work was supported by the Natural Science Foundation of Guangxi Province (2018GXNSFAA281218 and 2019GXNSFAA245017), the Innovation-Driven Development of Hezhou (Hekechuang PT0710004), the Undergraduate Teaching Reform Project for Higher Education of Guangxi Province (2019JGZ150), and the Science and Technology Major Project of Guangxi Province (AA18242006 and AA18242008).

ORCID iDs

Zhenming Chen

Tianliang Feng

References

Tressmann

DMGA

Pedroti

de Carvalho

, et al. Research into the use of marble waste as mineral filler in soil pigment-based paints and as an active pigment in waterborne paints. Construction Building Mater 2020; 241: 117976.

Hebhoub

Aoun

Belachia

, et al. Use of waste marble aggregates in concrete. Constr Build Mater 2011; 25: 1167–1171.

Ashish

. Feasibility of waste marble powder in concrete as partial substitution of cement and sand amalgam for sustainable growth. J Build Eng 2018; 15: 236–242.

Eliche-Quesada

Corpas-Iglesias

Pérez-Villarejo

, et al. Recycling of sawdust, spent earth from oil filtration, compost and marble residues for brick manufacturing. Constr Build Mater 2012; 34: 275–284.

Awad

El-gamasy

A Abd El-Wahab

, et al. Mechanical behavior of PP reinforced with marble dust. Construction Building Mater 2019; 228: 116766.

El-Alf

Gado

. Preparation of calcium sulfoaluminate-belite cement from marble sludge waste. Constr Build Mater 2016; 113: 764–772.

Nawar

Ghaedi

Ali

, et al. Recycling waste-derived marble powder for CO₂ capture. Process Saf Environ 2019; 132: 214–225.

Chen

Yang

, et al. Use of titanate to improve interfacial interaction and mechanical properties of polyethylene/artificial marble wastes composites. J Vinyl Addit Technol 2021; 27: 137–146.

Ahmed

Nizami

Raza

, et al. Effect of micro-sized marble sludge on physical properties of natural rubber composites. Chem Ind Chem Eng Q 2013; 19: 281–293.

10.

Çınar

Kar

. Characterization of composite produced from waste PET and marble dust. Constr Build Mater 2018; 163: 734–741.

11.

Cong

, et al. High strength artificial stoneware from marble waste via surface modification and low temperature sintering. J Clean Prod 2018; 180: 728–734.

12.

Awad

Abdellatif

. Assessment of mechanical and physical properties of LDPE reinforced with marble dust. Composites Part B: Eng 2019; 173: 106948.

13.

Khan

Patidar

Pappu

. Marble waste characterization and reinforcement in low density polyethylene composites via injection moulding: Towards improved mechanical strength and thermal conductivity. Construction Building Mater 2021; 269: 121229.

14.

Nayak

Satapathy

Mantry

. Processing and wear response study of glass-polyester composites with waste marble dust as particulate filler. Polym Compos 2020; 41: 2263–2273.

15.

Huang

Guo

Zhou

, et al. Poly(vinyl alcohol)/artificial marble wastes composites with improved melt processability and mechanical properties. Composites Part B: Eng 2020; 182: 107628.

16.

Durmaz

Ozturk

Aytac

. Reduced graphene oxide reinforced PET/PBT nanocomposites: compatibilization and characterization. Polym Eng Sci 2020; 60: 2606–2618.

17.

Kang

Niu

, et al. The crystallization, thermal and mechanical properties of nano-Sb2O3 filled poly(butylene terephthalate). J Vinyl Addit Technol 2020; 26: 268–281.

18.

Ganguly

Channe

Jha

, et al. Review on transesterification in polycarbonate–poly(butylene terephthalate) blend. Polym Eng Sci 2021; 61: 650–661.

19.

Arslan

Dogan

. The mechanical and thermal properties of chopped basalt fiber-reinforced poly(butylene terephthalate) composites: effect of fiber amount and length. J Compos Mater 2019; 53: 2465–2475.

20.

Xie

Giacomin

, et al. Suppressing shrinkage/warpage of PBT injection molded parts with fillers. Polym Compos 2018; 39: 2377–2384.

21.

Heidarzadeh

Rafizadeh

Taromi

, et al. Preparation of poly(butylene terephthalate)/modified organoclay nanocomposite via in-situ polymerization: characterization, thermal properties and flame retardancy. High Perform Polym 2012; 24: 589–602.

22.

Bian

Lin

, et al. Processing and assessment of high-performance poly(butylene terephthalate) nanocomposites reinforced with microwave exfoliated graphite oxide nanosheets. Eur Polym J 2013; 49: 1406–1423.

23.

, et al. Crystallization and thermal behavior of multiwalled carbon nanotube/poly(butylenes terephthalate) composites. Polym Eng Sci 2008; 48: 1057–1067.

24.

Chen

Wang

. Recycled carbon fiber reinforced poly(butylene terephthalate) thermoplastic composites: fabrication, crystallization behaviors and performance evaluation. Polym Adv Technol 2013; 24: 364–375.

25.

Tomar

Maiti

. Mechanical properties of PBT/ABAS blends. J Appl Polym Sci 2007; 104: 1807–1817.

26.

Song

Zhou

, et al. Influence of core–shell particles structure on the morphology and brittle-ductile transition of PBT/ABS-g-GMA blends. Polym Compos 2013; 34: 15–21.

27.

Wang

Chen

Zhang

. Effects of reactive compatibilizer on the core–shell structured modifiers toughening of poly(trimethylene terephthalate). Polymer 2009; 50: 1483–1490.

28.

Singh

Siddhartha . Mechanical and thermo-mechanical peculiarity of functionally graded materials-based glass fiber-filled polybutylene terephthalate composites. J Reinf Plast Compos 2018; 37: 410–426.

29.

Huang

, et al. Crystalline structures of poly(L-lactide) formed under pressure and structure transitions with heating. Crystengcomm 2013; 15: 4372–4378.

30.

Wang

Jiang

, et al. Study on the effect of polyFR and its FR system on the flame retardancy and foaming behavior of polystyrene. RSC Adv 2019; 9: 192–205.

31.

Tan

Wang

. Preparation, microstructures, and properties of long-glass-fiber-reinforced thermoplastic composites based on polycarbonate/poly(butylene terephthalate) alloys. J Reinf Plast Compos 2015; 34: 1804–1820.

32.

Tong

Zhang

, et al. Mechanical and thermal properties and crystallization behavior of PA66 composites reinforced with MWCNTs-coated milled glass fiber. High Perform Polym 2021; 33: 89–104.

33.

Luyt

Dramićanin

Antić

, et al. Morphology, mechanical and thermal properties of composites of polypropylene and nanostructured wollastonite filler. Polym Test 2009; 28: 348–356.

34.

Liao

, et al. Preparation and properties of polybutylene‐terephthalate/graphene oxide in situ flame‐retardant material. J Appl Polym Sci 2020; 137: 49214.

35.

Ahmetli

Kocak

Dag

, et al. Mechanical and thermal studies on epoxy toluene oligomer-modified epoxy resin/marble waste composites. Polym Compos 2012; 33: 1455–1463.

36.

Soudmand

Shelesh‐Nezhad

Salimi

. A combined differential scanning calorimetry‐dynamic mechanical thermal analysis approach for the estimation of constrained phases in thermoplastic polymer nanocomposites. J Appl Polym Sci 2020; 137: 49260.

37.

Lin

Liu

, et al. Rheological behavior, mechanical properties, and nonisothermal crystallization behavior of poly(ethylene terephthalate)/modified carbon fiber composites. High Perform Polym 2019; 31: 733–740.

38.

Taraghi

Fereidoon

Zamani

, et al. Mechanical, thermal, and viscoelastic properties of polypropylene/glass hybrid composites reinforced with multiwalled carbon nanotubes. J Compos Mater 2015; 49: 3557–3566.

39.

Hsu

Liao

. Nonisothermal crystallization behavior and crystalline structure of poly(3-hydroxybutyrate)/layered double hydroxide nanocomposites. J Polym Sci Pol Phys 2007; 45: 995–1002.

40.

Tang

Yang

, et al. Nonisothermal and isothermal crystallization behavior of isotactic polypropylene/chemically reduced graphene nanocomposites. Polym Compos 2017; 38: E342–E350.

41.

Avrami

. Kinetics of phase change. I general theory. J Chem Phys 1939; 7: 1103–1112.

42.

Avrami

. Kinetics of phase change. II transformation-time relations for random distribution of nuclei. J Chem Phys 1940; 8: 212–224.

43.

Sencadas

Costa

Ribelles

JLG

, et al. Isothermal crystallization kinetics of poly(vinylidene fluoride) in the α-phase in the scope of the avrami equation. J Mater Sci 2010; 45: 1328–1335.

44.

Ong

Chow

. Kinetics of crystallization for polypropylene/polyethylene/halloysite nanotube nanocomposites. J Thermoplast Compos Mater 2020; 33: 451–463.

45.

Gao

Chen

, et al. Electrically insulated epoxy nanocomposites reinforced with synergistic core-shell SiO2 @MWCNTs and montmorillonite bifillers. Macromolecular Chem Phys 2017; 218: 1700357.

46.

Kim

Yao

Han

, et al. Mechanical and physical properties of core–shell structured wood plastic composites: Effect of shells with hybrid mineral and wood fillers. Compos Part B: Eng 2013; 45: 1040–1048.

47.

Chen

, et al. Multilayered core–shell structure of the dispersed phase in high-impact polypropylene. J Appl Polym Sci 2008; 108: 2379–2385.

48.

Hassanien

MSS

. Mechanical and rheological properties of polypropylene (PP)/linear low density polyethylene (LLDPE) blend filled with talc and calcium carbonate compositions. Int J Eng Sci Res Technol 2015; 4: 383–387.

49.

Ferreira

EDB

Luna

CBB

Araujo

, et al. Polypropylene/wood powder composites: Evaluation of PP viscosity in thermal, mechanical, thermomechanical, and morphological characters. J Thermoplast Compos Mater 2022; 35: 71–92.

50.

Tehran

Shelesh-Nezhad

Barazandeh

. Mechanical and thermal properties of TPU-toughened PBT/CNT nanocomposites. J Thermoplast Compos Mater 2019; 32: 815–830.