*Article* **Investigation of Mechanical Properties for Basalt Fiber/Epoxy Resin Composites Modified with La**

**Chong Li 1,\*, Haoyu Wang 2,\*, Xiaolei Zhao <sup>3</sup> , Yudong Fu <sup>2</sup> , Xiaodong He <sup>4</sup> and Yiguo Song <sup>1</sup>**


**Abstract:** As an efficient reinforcing material in resin matric composites, the application of basalt fibers (BFs) in composites is limited by the poor interfacial adhesion between BFs and the resin matrix. In this study, to obtain the basalt fibers/epoxy resin composites with enhanced mechanical properties, the modification solution containing different concentrations of Lanthanum ions (La3+) was synthesized to modify the BFs surfaces to enhance the poor interfacial adhesion between BFs and the matrix. The morphology, the chemical structure and the chemical composition of the modified BFs surface were observed and detected by scanning electron microscopy, Fourier transform infrared spectroscopy and X-ray photoelectron spectroscopy, respectively. The results show that, after BFs were soaked in the modification solution, the more active groups (C=O, –OH, C–O, etc.) were introduced to the BFs surfaces and effectively enhanced the bond strength between BFs and the resin matrix. The obtained mechanical performances of prepared basalt fibers/epoxy resin composites showed that the tensile strength, bending strength and interlaminar shear strength (ILSS) were improved with the modified BFs, and reached to 458.7, 556.7 and 16.77 Mpa with the 0.5 wt.% La. Finally, the enhancement mechanism of the modification solution containing La element is analyzed.

**Keywords:** basalt fibers; composites; mechanical properties; surface engineering

#### **1. Introduction**

In the past years, many studies have been conducted on the applicability of basalt fibers (BFs). As a reinforcing material for composites, BFs (mainly composed by SiO2) can be prepared from basalt rocks using conventional equipment with the advantage on the low-cost process of melting and drawing [1]. Compared with other fiber materials, BFs have the excellent properties such as high tensile strength, high E-modulus, high abrasion strength, high temperature resistance, high resistance to aggressive media, excellent thermal and sound insulation, good chemical stability [2]. Moreover, the mechanical properties of BFs can be kept without significant decrease in the operating temperature range of 200–600 ◦C [3]. In addition, the environmentally friendly preparation and recycling process of BFs significantly improves its demand for the modern market [1,4–6]. Thus, the BFs might be a promising reinforced material as the candidate of glass and carbon fibers in composite materials, and have been attractive in the application of friction materials, corrosion resistance materials, heat shields, thermal insulting barriers and hot fluid transportation pipes in many fields [7].

Especially in the field of flywheel rotors' structural materials, the fiber-reinforced resin matrix composite flywheel was generally to replace the traditional metal flywheel due to

**Citation:** Li, C.; Wang, H.; Zhao, X.; Fu, Y.; He, X.; Song, Y. Investigation of Mechanical Properties for Basalt Fiber/Epoxy Resin Composites Modified with La. *Coatings* **2021**, *11*, 666. https://doi.org/10.3390/ coatings11060666

Academic Editor: Maude Jimenez

Received: 22 April 2021 Accepted: 29 May 2021 Published: 31 May 2021

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**Copyright:** © 2021 by the authors. Licensee MDPI, Basel, Switzerland. This article is an open access article distributed under the terms and conditions of the Creative Commons Attribution (CC BY) license (https:// creativecommons.org/licenses/by/ 4.0/).

their high strength, high energy storage density and low specific volume [8]. Compared with the common reinforced fibers (glass and carbon fibers), the BFs represent an alternative as the substitution due to their excellent properties.

However, the smooth and chemically inert surface of BFs [9–11] results in the low interfacial adhesion between BFs and matrix (here below referred as interfacial adhesion) to reduce the composite materials' performance. To enhance the interfacial adhesion, many studies have been conducted to modify the fiber surface, such as the plasma modification technology, the oxidized modification technology, the coating modification technology, and so on [12–23]. Manikandan and Jain et al. [3,24] increased the surface roughness of BFs by the acid and alkali chemical treatments, which improved interfacial bonding strength between fibers and matrix. Kim et al. [11] and Ricciardi [25] used surface treatment of BFs by low-temperature atmospheric oxygen plasma and SF<sup>6</sup> plasma to increase the wettability of BFs remarkably, and improve adhesive force between fiber/resin interfaces accompanied by physical etching and by the formation of chemical functional groups containing oxygen and nitrogen on the fiber surface. This increased the interlaminar fracture toughness of basalt/epoxy woven composites. Wei et al. proposed the coating modification as an effective way in improving the mechanical properties of BFs and the properties of basalt fiber/epoxy resin composites [1,6]. Cheng et al. [26–28] investigated the effects of surface-treated F-12 aramid fibers and carbon fibers on the interfacial adhesion between fibers and matrix. They found that rare earth modification solution treatment can increase the concentration of reactive functional groups on fiber surface through chemical coordinating reaction. Additionally, the interfacial adhesion was promoted obviously and the tensile properties of composites improved significantly. Meanwhile, the tensile strengths of single fibers are almost not affected by rare earth modification solution treatment. It exhibits an attractive method to treat BFs with the rare earth modification solution due to its high efficiency, simple process, environmentally friendly characteristics, and preservation of fiber tensile strengths. Thus, with the few studies on BFs modified by rare earth elements, the modification study on BFs to prepare fiber-reinforced composites with excellent performance was promising.

In this study, the rare earth modification solution was synthesized by adding different concentrations of element La. The effects of the BFs surfaces with different concentration of element La were investigated. The mechanical properties of the composite materials, such as the tensile strength, the bending strength and the interlaminar shear strength (ILSS) were detected. The modification mechanism of the BFs surface was also discussed.

#### **2. Experimental Details**

#### *2.1. Materials*

The used BFs cloth (223 g/km, unidirectional cloth) with an average fiber of diameter (5.9 µm) was manufactured by Shanxi Basalt Fiber Technology Co., Ltd., Taiyuan, China. The elastic modulus and the tensile strength of the BFs cloth were about 7.5 and 1835 MPa, respectively. The epoxy resin (LY564) and the curing agent (22964, aliphatic polyamine curing agent) were from Huntsman Co., Ltd. (The Woodlands, TX, USA). The following chemical reagents were used: acetone and nitric acid (analytical reagent, provided by Tianjin Tianda Chemical Reagent Factory, Tianjin, China), absolute ethyl alcohol (analytical reagent, produced by Tianjin Tianli Chemical Reagent Co., Ltd., Tianjin, China), citric acid and urea (analytical reagent, provided by Tianjin Zhiyuan Chemical Reagent Co., Ltd., Tianjin, China), lanthanum chloride (99.99%, manufactured by Jining Zhongkai New Type Material Co., Ltd., Jining, China).

#### *2.2. Treatment of Fibers*

The BFs cloth was cut into 260 <sup>×</sup> 35 mm<sup>2</sup> . After immersed in acetone for 48 h at room temperature to remove the protective coating on the surface of BFs, the fibers were dried in a drying oven at 100 ◦C for 1 h. The dried fiber cloth was soaked in the concentrated nitric acid with constant temperature water bath at 60 ◦C for 2 h to improve the roughness and

the –OH numbers of the fibers' surfaces [29]. Washing the fibers 3–4 times with distilled water to remove acid fluid from their surfaces, the PH value on the surface of the fibers was adjusted to 7. Finally, the fibers were dried in a drying oven at 100 ◦C for 1 h and conserved in the dryer.

According to a certain weight ratio, the composition of the BFs modification solution were uniformly mixed at room temperature, as shown in Table 1. Additionally, five kinds of rare earth modification solution were prepared with different La3+ concentrations of 0.1, 0.3, 0.5, 0.7, and 0.9 wt.% After immersed in the rare earth modification solution for 2 h, the treated BFs were dried in the drying oven at 100 ◦C for 1 h.

**Table 1.** Composition of the BFs modification solution.


#### *2.3. Fabrication and Measurements of Basalt Fiber/Epoxy Resin Composites*

The prepared BFs was immersed in epoxy resin/curing agent mixture at volume ratio 4:1. With the hand lay-up method, the BF/ERCs were paved as three layers in the mold, and fabricated after curing in a drying oven at 120 ◦C for 15 min and 140 ◦C for 2 h, respectively.

The change of BFs' chemical structure was determined in the transmission mode using Fourier transform infrared spectroscopy (FT-IR, Perkin Elmer 100, Waltham, MA, USA). X-ray photoelectron spectroscopy (XPS) using a PHI 5700 ESCA System equipped with an Al-Ka X-ray source (NewYork, NY, USA), analyzed the chemical composition of the BFs surfaces. The surface morphologies of BFs and the fracture surface morphologies of the composites were examined using scanning electron microscopy (SEM, JSM-6480, Tokyo, Japan).

The tensile test and the bending test were carried out to determine the tensile strength and the bending strength of BF/ERCs, respectively. The ILSS of BF/ERCs was measured by the three-point short-beam bending test. Due to the details of the mechanical tests shown in Table 2 below, the specimens were cut according to the following dimensional requirement.



#### **3. Results**

#### *3.1. FT-IR Spectra of BFs*

The chemical structures of untreated and treated BFs were obtained with FT-IR spectroscopy, as shown in Figure 1. The characteristic peaks of –OH at 3450 cm−<sup>1</sup> and C=O at 1630 cm−<sup>1</sup> were observed in the untreated BFs. In addition, the peaks of –CH<sup>2</sup> appeared at 2921 and 2844 cm−<sup>1</sup> , respectively. As the main composition of BFs, the peak of Si-O from SiO<sup>2</sup> of BFs appeared at 860 cm−<sup>1</sup> .

**3. Results** 

*3.1. FT-IR Spectra of BFs* 

the loss of active groups.

SiO2 of BFs appeared at 860 cm−1.

The chemical structures of untreated and treated BFs were obtained with FT-IR spec-

For BFs treated with the 0.1 wt.% La3+ rare earth modification solution, the new ab-

With the La3+ concentration above 0.5 wt.%, the peak of C=O began to disappear. At

the La3+ concentration of 0.9 wt.%, the peak disappearances of C–O at 1260 cm−1 and the other weakened characteristic peaks were observed, implying that superabundant active groups introduced by the excess La3+ were aggregated on the BFs to be supersaturated and further destroyed formed macromolecular membrane on the BFs' surface to trigger

sorption peaks of C=O at 1660 cm−1 and –OH at 1384 cm−1 appeared in the range of 4000– 1330 cm−1, and the peaks of –CH2 at 2917 and 2845 cm−1 from the citric acid were broader than those of the untreated BFs, indicating that the La3+ was successfully absorbed on the BFs' surface with the introduced –CH2– from the acyl group and citric acid, which also brought C=O. The absorption band at the peak of 1046 cm−1 referred to the formation of along with the peak of shifting from 860 to 863cm−1, stating that the Si–OH from the hydrolysis of SiO2 react with itself or the introduced –COOH under dehydration condensation reaction to produce Si–O–Si and more Si–O. With La3+ concentration increasing to 0.3 wt.% in the rare earth modification solution, the new peak of C–O from the citric acid along with the introduced La3+ at 1116 cm−1 appeared in the FT-IR spectrum. Moreover, the peaks of –CH2 at 2922 and 2859 cm−1 exhibited obviously. It indicated that the La3+ was absorbed to the surface with –COOH and –CH2 from citric acid. When La3+ concentration was up to 0.5 wt.%, the vibration frequency of C–O increased from 1116 to 1260 cm−1, and that of C=O stretched from 1668 to 1716 cm−1, accompanied by the urea in the modification solution. Due to the strong affinity of La3+ to nonmetal element, the La3+ could combine with urea and citric acid under the coordination reaction to introduce the C=O and C–O from the modification solution, resulting that more active oxygen-contained functional groups were introduced onto the fiber surfaces with the increasing La3+ concentration.

troscopy, as shown in Figure 1. The characteristic peaks of –OH at 3450 cm−1 and C=O at 1630 cm−1 were observed in the untreated BFs. In addition, the peaks of –CH2 appeared at 2921 and 2844 cm−1, respectively. As the main composition of BFs, the peak of Si-O from

**Figure 1.** FT-IR spectra of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%. **Figure 1.** FT-IR spectra of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

For BFs treated with the 0.1 wt.% La3+ rare earth modification solution, the new absorption peaks of C=O at 1660 cm−<sup>1</sup> and –OH at 1384 cm−<sup>1</sup> appeared in the range of 4000–1330 cm−<sup>1</sup> , and the peaks of –CH<sup>2</sup> at 2917 and 2845 cm−<sup>1</sup> from the citric acid were broader than those of the untreated BFs, indicating that the La3+ was successfully absorbed on the BFs' surface with the introduced –CH2– from the acyl group and citric acid, which also brought C=O. The absorption band at the peak of 1046 cm−<sup>1</sup> referred to the formation of along with the peak of shifting from 860 to 863cm−<sup>1</sup> , stating that the Si–OH from the hydrolysis of SiO<sup>2</sup> react with itself or the introduced –COOH under dehydration condensation reaction to produce Si–O–Si and more Si–O. With La3+ concentration increasing to 0.3 wt.% in the rare earth modification solution, the new peak of C–O from the citric acid along with the introduced La3+ at 1116 cm−<sup>1</sup> appeared in the FT-IR spectrum. Moreover, the peaks of –CH<sup>2</sup> at 2922 and 2859 cm−<sup>1</sup> exhibited obviously. It indicated that the La3+ was absorbed to the surface with –COOH and –CH<sup>2</sup> from citric acid. When La3+ concentration was up to 0.5 wt.%, the vibration frequency of C–O increased from 1116 to 1260 cm−<sup>1</sup> , and that of C=O stretched from 1668 to 1716 cm−<sup>1</sup> , accompanied by the urea in the modification solution. Due to the strong affinity of La3+ to nonmetal element, the La3+ could combine with urea and citric acid under the coordination reaction to introduce the C=O and C–O from the modification solution, resulting that more active oxygen-contained functional groups were introduced onto the fiber surfaces with the increasing La3+ concentration.

With the La3+ concentration above 0.5 wt.%, the peak of C=O began to disappear. At the La3+ concentration of 0.9 wt.%, the peak disappearances of C–O at 1260 cm−<sup>1</sup> and the other weakened characteristic peaks were observed, implying that superabundant active groups introduced by the excess La3+ were aggregated on the BFs to be supersaturated and further destroyed formed macromolecular membrane on the BFs' surface to trigger the loss of active groups.

#### *3.2. XPS Results of BFs 3.2. XPS Results of BFs*

#### 3.2.1. XPS Results of BFs 3.2.1. XPS Results of BFs

As shown in Figure 2 and Table 3, the XPS survey spectra and the detected atomic concentration of the elements C, O, N and Si on the BFs surfaces were respectively obtained to analyze the chemical composition of the BFs surface. On the surfaces of BFs treated with the rare earth modification solution, the concentration of element C decreased and then increased with the increase of La3+ concentration, but the changes of the elements O and N were contrary. The proportions of O/C and N/C on the BFs surfaces had the same variation trend with the concentration of element C. When La3+ concentration was 0.5 wt.%, the proportions of O/C and N/C reached maximum values, confirming that the BFs surfaces contained the largest number of active oxygen-containing groups. As shown in Figure 2 and Table 3, the XPS survey spectra and the detected atomic concentration of the elements C, O, N and Si on the BFs surfaces were respectively obtained to analyze the chemical composition of the BFs surface. On the surfaces of BFs treated with the rare earth modification solution, the concentration of element C decreased and then increased with the increase of La3+ concentration, but the changes of the elements O and N were contrary. The proportions of O/C and N/C on the BFs surfaces had the same variation trend with the concentration of element C. When La3+ concentration was 0.5 wt.%, the proportions of O/C and N/C reached maximum values, confirming that the BFs surfaces contained the largest number of active oxygen-containing groups.

**Figure 2.** XPS survey spectra of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.% **Figure 2.** XPS survey spectra of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.


**Table 3.** XPS results of BFs.

#### 3.2.2. XPS Results of La on BFs Surfaces

The fitted curves of La3d spectra on BFs surface treated with different modification solution containing La3+ are presented in Figure 3. The spectra peaks of La3d in the treated BFs with the different La3+ modification solution concentrations (0.1, 0.3, 0.5, 0.7, and 0.9 wt.%) were corresponding to the bonding energies of 851.02, 851.77, 851.9, 852, and 852.1 ev, respectively. All the bonding energies were lower than that (853.0 ev) of the La corresponding to La3d in LaCl3, indicating that the coordination chemical reactions occurred between the La and the O, C, N element of the treated fibers' surfaces to the generate lanthanum coordination compounds on fibers' surfaces.

#### 3.2.3. XPS Characterization of Element C on BFs Surfaces

The fitted curves of C 1*s* spectra and the detected functional groups contents on the BFs surfaces are presented in Figure 4 and Table 4, respectively. Three small peaks of C–C, C–O– and C=O appeared under the C 1*s* peak of the untreated BFs surfaces in Figure 4a, indicating that C atoms were combined with O atoms. The percentage of C atoms in the corresponding chemical state was represented with the area ratio of every small peak to the C 1*s* peak. Due to the low content of element N on BFs surfaces, the C–N bond could be ignored.

As seen in Figure 4b, with the peak appearance of –COOH in the fitted curves of C 1*s* spectra of the BFs, new functional groups were generated on the surface of BFs treated with the rare earth modification solution, besides the original ones. According to the low-to-high order of binding energy, these functional groups can be arranged as alcoholic hydroxyl (C–OH) or ether bond (C–O–C), carbonyl (C=O) and carboxyl (COOH). The –C–C content on the BFs surfaces firstly decreased and then increased with La3+ concentration increasing, but the changes of the carbon–oxygen bond were contrary. When La3+ concentration was 0.5 wt.%, with the sum of C–OH/–C–O–C–, C=O and –COOH reaching to a maximum value (72.87%), the number of oxygen-containing groups on the BFs surfaces were the largest. As La3+ concentration exceeded 0.5 wt.%, the content of carbon–oxygen bond decreased. That was attributed to the fact that the abundant oxygen-containing groups introduced by excess La were aggregated on the fibers' surfaces and could not be stably absorbed to the fibers' surfaces with the weak Van der Waals force between La3+. Moreover, the aggregated supersaturated active oxygen-containing groups could also trigger the break of the origin formed macromolecular membrane on the fibers' surfaces, which led to the loss of active groups.

**Table 3.** XPS results of BFs.

3.2.2. XPS Results of La on BFs Surfaces

**Specimens Elements (%) O/C N/C** C O Si N La

Untreated 80.65 15.06 2.47 0.78 - 0.19 0.01 0.1 wt.% La3+ 65.29 25.55 5.38 3.72 0.07 0.39 0.06 0.3 wt.% La3+ 56.14 28.62 5.59 7.63 0.22 0.51 0.14 0.5 wt.% La3+ 40.95 43.38 5.78 9.01 0.88 1.05 0.22 0.7 wt.% La3+ 50.42 33.97 6.31 8.36 0.94 0.67 0.17 0.9 wt.% La3+ 53.38 28.68 8.15 8.32 1.47 0.54 0.16

The fitted curves of La3d spectra on BFs surface treated with different modification solution containing La3+ are presented in Figure 3. The spectra peaks of La3d in the treated BFs with the different La3+ modification solution concentrations (0.1, 0.3, 0.5, 0.7, and 0.9 wt.%) were corresponding to the bonding energies of 851.02, 851.77, 851.9, 852, and 852.1 ev, respectively. All the bonding energies were lower than that (853.0 ev) of the La corresponding to La3d in LaCl3, indicating that the coordination chemical reactions occurred between the La and the O, C, N element of the treated fibers' surfaces to the gen-

erate lanthanum coordination compounds on fibers' surfaces.

**Figure 3.** XPS survey spectra of La on BFs surfaces: (**a**) treated with modification solution containing La3+ 0.1 wt.%; (**b**) treated with modification solution containing La3+ 0.3 wt.%; (**c**) treated with modification solution containing La3+ 0.5 wt.%; (**d**) treated with modification solution containing La3+ 0.7 wt.%; (**e**) treated with modification solution containing La3+ 0.9 wt.%. **Figure 3.** XPS survey spectra of La on BFs surfaces: (**a**) treated with modification solution containing La3+ 0.1 wt.%; (**b**) treated with modification solution containing La3+ 0.3 wt.%; (**c**) treated with modification solution containing La3+ 0.5 wt.%; (**d**) treated with modification solution containing La3+ 0.7 wt.%; (**e**) treated with modification solution containing La3+ 0.9 wt.%.

3.2.3. XPS Characterization of Element C on BFs Surfaces

which led to the loss of active groups.

C-C

0

2000

4000

6000

Intensity/Counts

COOH C=O

8000

10000

12000

(b)

be ignored.

294 292 290 288 286 284 282 280 278 276

Binding Energy /ev

C-OH/C-O-C

C=O

(a)

Intensity/Counts

The fitted curves of C 1*s* spectra and the detected functional groups contents on the BFs surfaces are presented in Figure 4 and Table 4, respectively. Three small peaks of C–C, C–O– and C=O appeared under the C 1*s* peak of the untreated BFs surfaces in Figure

the corresponding chemical state was represented with the area ratio of every small peak to the C 1*s* peak. Due to the low content of element N on BFs surfaces, the C–N bond could

As seen in Figure 4b, with the peak appearance of –COOH in the fitted curves of C 1*s* spectra of the BFs, new functional groups were generated on the surface of BFs treated with the rare earth modification solution, besides the original ones. According to the lowto-high order of binding energy, these functional groups can be arranged as alcoholic hydroxyl (C–OH) or ether bond (C–O–C), carbonyl (C=O) and carboxyl (COOH). The –C–C content on the BFs surfaces firstly decreased and then increased with La3+ concentration increasing, but the changes of the carbon–oxygen bond were contrary. When La3+ concentration was 0.5 wt.%, with the sum of C–OH/–C–O–C–, C=O and –COOH reaching to a maximum value (72.87%), the number of oxygen-containing groups on the BFs surfaces were the largest. As La3+ concentration exceeded 0.5 wt.%, the content of carbon–oxygen bond decreased. That was attributed to the fact that the abundant oxygen-containing groups introduced by excess La were aggregated on the fibers' surfaces and could not be stably absorbed to the fibers' surfaces with the weak Van der Waals force between La3+. Moreover, the aggregated supersaturated active oxygen-containing groups could also trigger the break of the origin formed macromolecular membrane on the fibers' surfaces,

294 292 290 288 286 284 282 280 278 276

Binding Energy /ev

C-OH/C-O-C

C-C

**BFs** 

**Area Ratio (%)** 

**Binding Energy (ev)** 

which led to the loss of active groups.

**Figure 3.** XPS survey spectra of La on BFs surfaces: (**a**) treated with modification solution containing La3+ 0.1 wt.%; (**b**) treated with modification solution containing La3+ 0.3 wt.%; (**c**) treated with modification solution containing La3+ 0.5 wt.%; (**d**) treated with modification solution containing La3+ 0.7 wt.%; (**e**) treated with modification solution containing La3+ 0.9 wt.%.

**870 860 850 840 830 820**

La3d

Bending energy/ev

3.2.3. XPS Characterization of Element C on BFs Surfaces

be ignored.

**5000**

**5500**

**6000**

**6500**

Intensity/a.u

**7000**

**7500**

(e) 852.1ev

The fitted curves of C 1*s* spectra and the detected functional groups contents on the BFs surfaces are presented in Figure 4 and Table 4, respectively. Three small peaks of C–C, C–O– and C=O appeared under the C 1*s* peak of the untreated BFs surfaces in Figure 4a, indicating that C atoms were combined with O atoms. The percentage of C atoms in the corresponding chemical state was represented with the area ratio of every small peak to the C 1*s* peak. Due to the low content of element N on BFs surfaces, the C–N bond could

As seen in Figure 4b, with the peak appearance of –COOH in the fitted curves of C 1*s* spectra of the BFs, new functional groups were generated on the surface of BFs treated with the rare earth modification solution, besides the original ones. According to the lowto-high order of binding energy, these functional groups can be arranged as alcoholic hydroxyl (C–OH) or ether bond (C–O–C), carbonyl (C=O) and carboxyl (COOH). The –C–C content on the BFs surfaces firstly decreased and then increased with La3+ concentration increasing, but the changes of the carbon–oxygen bond were contrary. When La3+ concentration was 0.5 wt.%, with the sum of C–OH/–C–O–C–, C=O and –COOH reaching to a maximum value (72.87%), the number of oxygen-containing groups on the BFs surfaces were the largest. As La3+ concentration exceeded 0.5 wt.%, the content of carbon–oxygen bond decreased. That was attributed to the fact that the abundant oxygen-containing groups introduced by excess La were aggregated on the fibers' surfaces and could not be stably absorbed to the fibers' surfaces with the weak Van der Waals force between La3+. Moreover, the aggregated supersaturated active oxygen-containing groups could also trigger the break of the origin formed macromolecular membrane on the fibers' surfaces,

**Figure 4.** Fitted curves of C1s spectra: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.% **Figure 4.** Fitted curves of C1s spectra: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

**Table 4.** C 1*s* results of BFs surfaces.

**–C–C C–OH/–C–O–C– C=O –COOH** 

**Area Ratio (%)** 

The functional group contents on the BFs surfaces are presented in Table 5, according to the fitted curves of Si 2*p* spectra in Figure 5. Figure 5a showed that SiO2 and Si–O–Si bonds appeared on the untreated BFs surfaces, affirming that SiO2 was the main chemical composition of BFs surfaces. The existence of Si–O–Si bonds was ascribed to the formation of BFs connected by [SiO4] tetrahedron, which could further form [Si2O7] under interaction and even the chain structure with a higher degree of polymerization. Under the hydrolysis of SiO2 in the modification solution, the new functional group (Si–OH) was generated on the surface of BFs treated with the rare earth modification solution along with the obvious decrease of SiO2. However, the increase of Si–O–Si was mainly ascribed to the dehydration condensation reaction of Si–OH bonds by themselves or active organic groups in the mod-

**Binding Energy (ev)** 

**Area Ratio (%)** 

**Binding Energy (ev)** 

0.1 wt.% La3+ 41.89 284.33 21.23 285.15 20.56 286.473 16.32 288.89 0.3 wt.% La3+ 30.41 284.23 30.98 284.88 23.37 286.1 15.23 288.66 0.5 wt.% La3+ 27.13 284.52 27.36 284.87 24.56 286.43 20.96 288.8 0.7 wt.% La3+ 39.23 284.45 22.76 285.3 17.80 286.44 20.21 288.7 0.9 wt.% La3+ 42.18 284.37 22.98 285.11 15.35 286.29 19.49 288.6

3.2.4. XPS Characterization of Si Element on BFs Surfaces

ification solution, such as –COOH and –OH.

**Binding En-**

**Area Ratio (%)** 


**Table 4.** C 1*s* results of BFs surfaces.

3.2.4. XPS Characterization of Si Element on BFs Surfaces

The functional group contents on the BFs surfaces are presented in Table 5, according to the fitted curves of Si 2*p* spectra in Figure 5. Figure 5a showed that SiO<sup>2</sup> and Si–O–Si bonds appeared on the untreated BFs surfaces, affirming that SiO<sup>2</sup> was the main chemical composition of BFs surfaces. The existence of Si–O–Si bonds was ascribed to the formation of BFs connected by [SiO4] tetrahedron, which could further form [Si2O7] under interaction and even the chain structure with a higher degree of polymerization. Under the hydrolysis of SiO<sup>2</sup> in the modification solution, the new functional group (Si–OH) was generated on the surface of BFs treated with the rare earth modification solution along with the obvious decrease of SiO2. However, the increase of Si–O–Si was mainly ascribed to the dehydration condensation reaction of Si–OH bonds by themselves or active organic groups in the modification solution, such as –COOH and –OH.

**Table 5.** Si 2*p* results of BFs surfaces.


It can be seen that the SiO2 content on the BFs surfaces firstly decreased and then

increased with La3+ concentration increasing, but the content changes of Si–O–Si and Si– OH were contrary. When La3+ concentration was 0.5 wt.%, the SiO2 content reached a minimum value (36.12%) corresponding to the highest contents of Si–O–Si and Si–OH. With the La3+ concentration beyond 0.5 wt.%, the ether bond was generated with the reaction of Si–OH and active groups in the rare earth modification solution. Accordingly, the hy-

drolysis of SiO2 was compressed and the content of SiO2 increased.

**Figure 5.** Fitted curves of Si element spectra: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.% **Figure 5.** Fitted curves of Si element spectra: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

It can be seen that the SiO<sup>2</sup> content on the BFs surfaces firstly decreased and then increased with La3+ concentration increasing, but the content changes of Si–O–Si and Si–OH were contrary. When La3+ concentration was 0.5 wt.%, the SiO<sup>2</sup> content reached a minimum value (36.12%) corresponding to the highest contents of Si–O–Si and Si–OH. With the La3+ concentration beyond 0.5 wt.%, the ether bond was generated with the reaction of Si–OH and active groups in the rare earth modification solution. Accordingly, the hydrolysis of SiO<sup>2</sup> was compressed and the content of SiO<sup>2</sup> increased. 0.7 wt.% La3+ 51.80 105.97 27.32 103.25 20.88 102.18 0.9 wt.% La3+ 58.13 105.71 23.89 103.17 17.98 102.28 *3.3. Basalt Fiber Surface Morphology*  Figure 6 reveals the changes of BFs surface morphology after modification. The surfaces of untreated BFs were smooth without obvious grooves or salients in Figure 6a. Some particles formed through the process of the active groups drawn onto the fiber sur-

**Area Ratio (%)** 

Untreated 71.14 102.59 28.86 101.75 - - 0.1 wt.% La3+ 47.41 106.16 33.64 103.48 18.94 102.43 0.3 wt.% La3+ 40.15 105.85 36.81 103.37 23.04 102.47 0.5 wt.% La3+ 36.12 105.81 39.72 103.28 24.17 102.33

**SiO2 Si–O–Si Si–OH** 

**Binding Energy (ev)** 

**Area Ratio (%)** 

**Binding Energy (ev)** 

#### *3.3. Basalt Fiber Surface Morphology* faces by the rare earth element, were attached to the surfaces of BFs treated with the rare earth modification solution containing La3+ concentration 0.1 wt.% in Figure 6b. Figure

**Table 5.** Si 2*p* results of BFs surfaces.

**Area Ratio (%)** 

**BFs** 

*Coatings* **2021**, *11*, 666 10 of 18

**Binding Energy (ev)** 

Figure 6 reveals the changes of BFs surface morphology after modification. The surfaces of untreated BFs were smooth without obvious grooves or salients in Figure 6a. Some particles formed through the process of the active groups drawn onto the fiber surfaces by the rare earth element, were attached to the surfaces of BFs treated with the rare earth modification solution containing La3+ concentration 0.1 wt.% in Figure 6b. Figure 6c,d shows that a trend of increasing particles was accompanied by an increasing concentration of La3+. When La3+ concentration was up to 0.5 wt.%, a great number of small particles uniformly covered the fiber surfaces to form the fibers' coatings. 6c,d shows that a trend of increasing particles was accompanied by an increasing concentration of La3+. When La3+ concentration was up to 0.5 wt.%, a great number of small particles uniformly covered the fiber surfaces to form the fibers' coatings. As shown in Figure 6e,f, the particles decreased on the fiber surfaces, as La3+ concentration increased to 0.7 wt.%. When La3+ concentration was up to 0.9 wt.%, the excess rare earth elements were attached onto the fiber surfaces with the saturation of active groups, resulting that only a few particles of inhomogeneous size were on the fibers. Moreover, these active groups were easy to bulge and even be broken under the function of tension.

**Figure 6.** SEM images of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

> As shown in Figure 6e,f, the particles decreased on the fiber surfaces, as La3+ concentration increased to 0.7 wt.%. When La3+ concentration was up to 0.9 wt.%, the excess rare earth elements were attached onto the fiber surfaces with the saturation of active groups,

resulting that only a few particles of inhomogeneous size were on the fibers. Moreover, these active groups were easy to bulge and even be broken under the function of tension. 0.5 wt.%. The active functional groups attached to the fibers' surfaces, such as C=O and O–H, improved the fiber surface roughness and activity, and thus enhanced the adhesion between fibers and the composite matrix. The maximum values of the tensile strength, the between fibers and the composite matrix. The maximum values of the tensile strength, the bending strength and ILSS were up to 458.7, 556.7 and 16.77 Mpa, and increased by

Tensile, bending and ILSS standard tests were performed to analyze mechanical behavior of BF/ERCs. According to the obtained experimental data shown in Figures 7–9, the mechanical properties, including the tensile strength, the bending strength and ILSS of BF/ERCs, were improved by BFs treated with La3+ concentration increasing from 0.1 to

havior of BF/ERCs. According to the obtained experimental data shown in Figures 7–9, the mechanical properties, including the tensile strength, the bending strength and ILSS of BF/ERCs, were improved by BFs treated with La3+ concentration increasing from 0.1 to 0.5 wt.%. The active functional groups attached to the fibers' surfaces, such as C=O and O–H, improved the fiber surface roughness and activity, and thus enhanced the adhesion

Tensile, bending and ILSS standard tests were performed to analyze mechanical be-

*Coatings* **2021**, *11*, 666 11 of 18

*Coatings* **2021**, *11*, 666 11 of 18

**Figure 6.** SEM images of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated

**Figure 6.** SEM images of BFs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated

*3.4. Mechanical Properties of Basalt Fibers/Epoxy Resin Composites* 

*3.4. Mechanical Properties of Basalt Fibers/Epoxy Resin Composites* 

with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

#### *3.4. Mechanical Properties of Basalt Fibers/Epoxy Resin Composites* bending strength and ILSS were up to 458.7, 556.7 and 16.77 Mpa, and increased by 56.22%, 103.32% and 88% compared with those of the unmodified ones, respectively.

Tensile, bending and ILSS standard tests were performed to analyze mechanical behavior of BF/ERCs. According to the obtained experimental data shown in Figures 7–9, the mechanical properties, including the tensile strength, the bending strength and ILSS of BF/ERCs, were improved by BFs treated with La3+ concentration increasing from 0.1 to 0.5 wt.%. The active functional groups attached to the fibers' surfaces, such as C=O and O–H, improved the fiber surface roughness and activity, and thus enhanced the adhesion between fibers and the composite matrix. The maximum values of the tensile strength, the bending strength and ILSS were up to 458.7, 556.7 and 16.77 Mpa, and increased by 56.22%, 103.32% and 88% compared with those of the unmodified ones, respectively. 56.22%, 103.32% and 88% compared with those of the unmodified ones, respectively. When La3+ concentration exceeded 0.5 wt.%, the mechanical strength of composites decreased as La3+ concentration increased. This may be ascribed to the fact that the excess active groups introduced by La3+ were aggregated to be supersaturated, and the triggered break of saturated active groups happened, leading to the loss of active groups. Moreover, the bits of grains on the interface of composite formed by the introduction of the excess La3+ to the fibers' surface also reduced the interface bonding strength. When La3+ concentration exceeded 0.5 wt.%, the mechanical strength of composites decreased as La3+ concentration increased. This may be ascribed to the fact that the excess active groups introduced by La3+ were aggregated to be supersaturated, and the triggered break of saturated active groups happened, leading to the loss of active groups. Moreover, the bits of grains on the interface of composite formed by the introduction of the excess La3+ to the fibers' surface also reduced the interface bonding strength.

**Figure 7.** Tensile strength of BF/ERCs. **Figure 7.** Tensile strength of BF/ERCs. **Figure 7.** Tensile strength of BF/ERCs.

**Figure 8.** Flexural strength of BF/ERCs. **Figure 8.** Flexural strength of BF/ERCs. **Figure 8.** Flexural strength of BF/ERCs.

**Figure 9.** ILSS of BF/ERCs. **Figure 9.** ILSS of BF/ERCs.

*3.5. Fracture Surfaces Morphology of Basalt Fibers/Epoxy Resin Composites*  The fracture surfaces of untreated and treated BF/ERCs in the tensile test was observed by SEM. In Figure 10a, smooth fibers and grooves can be seen on the fracture surfaces of untreated composites. Caused by the worse interfacial adhesion between fibers When La3+ concentration exceeded 0.5 wt.%, the mechanical strength of composites decreased as La3+ concentration increased. This may be ascribed to the fact that the excess active groups introduced by La3+ were aggregated to be supersaturated, and the triggered break of saturated active groups happened, leading to the loss of active groups. Moreover, the bits of grains on the interface of composite formed by the introduction of the excess La3+ to the fibers' surface also reduced the interface bonding strength.

#### and the resin matrix, the fibers can be easily separated or pulled out from the resin matrix, *3.5. Fracture Surfaces Morphology of Basalt Fibers/Epoxy Resin Composites*

exhibiting the low tensile strength of composites. There were a few resins on the fiber surfaces of composites treated with the rare earth modification solution containing La3+ concentration 0.1 wt.%, as shown in Figure 10b. Resins increased and grooves decreased on the fracture surfaces with the increase of La3+ concentration, as seen in Figure 10c,d. These residual resins on the fibers' surfaces were at-The fracture surfaces of untreated and treated BF/ERCs in the tensile test was observed by SEM. In Figure 10a, smooth fibers and grooves can be seen on the fracture surfaces of untreated composites. Caused by the worse interfacial adhesion between fibers and the resin matrix, the fibers can be easily separated or pulled out from the resin matrix, exhibiting the low tensile strength of composites.

tributed in the improved adhesion between fibers and the resin matrix, when fibers were stretched from the resin matrix under the stress. When La3+ concentration was up to 0.5 wt.%, the gaps between fibers were filled with the resins in Figure 10d. BFs and the resin matrix adhered so tightly that external load was delivered to the fibers from the matrix, and the fibers mainly tolerated the breaking stress. It exhibited the obviously improved mechanical properties of BF/ERCs in the better reinforcing effect. When La3+ concentration exceeded 0.5 wt.%, the decrease in resins on the fiber sur-There were a few resins on the fiber surfaces of composites treated with the rare earth modification solution containing La3+ concentration 0.1 wt.%, as shown in Figure 10b. Resins increased and grooves decreased on the fracture surfaces with the increase of La3+ concentration, as seen in Figure 10c,d. These residual resins on the fibers' surfaces were attributed in the improved adhesion between fibers and the resin matrix, when fibers were stretched from the resin matrix under the stress. When La3+ concentration was up to 0.5 wt.%, the gaps between fibers were filled with the resins in Figure 10d. BFs and the resin matrix adhered so tightly that external load was delivered to the fibers from the matrix, and the fibers mainly tolerated the breaking stress. It exhibited the obviously improved mechanical properties of BF/ERCs in the better reinforcing effect.

faces with increasing La3+ concentration led to the reappeared grooves on the resin matrix, when the smooth fibers pulled out, as seen in Figure 10 e,f. It demonstrated that the interfacial strength between the fibers and the resin matrix reduced, and the mechanical properties of composites correspondingly decreased. When La3+ concentration exceeded 0.5 wt.%, the decrease in resins on the fiber surfaces with increasing La3+ concentration led to the reappeared grooves on the resin matrix, when the smooth fibers pulled out, as seen in Figure 10e,f. It demonstrated that the interfacial strength between the fibers and the resin matrix reduced, and the mechanical properties of composites correspondingly decreased.

**Figure 9.** ILSS of BF/ERCs.

8

10

12

ILSS(Mpa)

14

16

18

*3.5. Fracture Surfaces Morphology of Basalt Fibers/Epoxy Resin Composites* 

0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0

solution concentration(wt%)

mechanical properties of BF/ERCs in the better reinforcing effect.

exhibiting the low tensile strength of composites.

erties of composites correspondingly decreased.

The fracture surfaces of untreated and treated BF/ERCs in the tensile test was observed by SEM. In Figure 10a, smooth fibers and grooves can be seen on the fracture surfaces of untreated composites. Caused by the worse interfacial adhesion between fibers and the resin matrix, the fibers can be easily separated or pulled out from the resin matrix,

There were a few resins on the fiber surfaces of composites treated with the rare earth modification solution containing La3+ concentration 0.1 wt.%, as shown in Figure 10b. Resins increased and grooves decreased on the fracture surfaces with the increase of La3+ concentration, as seen in Figure 10c,d. These residual resins on the fibers' surfaces were attributed in the improved adhesion between fibers and the resin matrix, when fibers were stretched from the resin matrix under the stress. When La3+ concentration was up to 0.5 wt.%, the gaps between fibers were filled with the resins in Figure 10d. BFs and the resin matrix adhered so tightly that external load was delivered to the fibers from the matrix, and the fibers mainly tolerated the breaking stress. It exhibited the obviously improved

When La3+ concentration exceeded 0.5 wt.%, the decrease in resins on the fiber surfaces with increasing La3+ concentration led to the reappeared grooves on the resin matrix, when the smooth fibers pulled out, as seen in Figure 10 e,f. It demonstrated that the interfacial strength between the fibers and the resin matrix reduced, and the mechanical prop-

**Figure 10.** SEM images of fracture surfaces of BF/ERCs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.% **Figure 10.** SEM images of fracture surfaces of BF/ERCs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution containing La3+ 0.9 wt.%.

The monomolecular layer theory can be supplemented to analyze the effect of element La concentration on the tensile performances of BF/ERCs with the model shown in Figure 11. At low concentrations, few La3+ were absorbed onto the BFs surfaces. As shown in Figure 11a, the arrangement of La atoms on BFs surfaces was discontinuous with a lot of voids, resulting in the failure of BF/ERCs occurring firstly on the location without La atoms under external load. Thus, the discontinuous interface between BFs and the epoxy resin is insufficient to improve the mechanical performance of BF/ERCs obviously. When La element increased to the best concentration, 0.5 wt.%, the uniform and compact monomolecular layer on the BFs surfaces exhibits high adhesive strength between BFs and the matrix, as shown in Figure 11b. The mechanical performances of BF/ERCs reached to the highest value, including the tensile strength, the bending strength, and ILSS. When La3+ concentration exceeded 0.5 wt.%, excessive La atoms were assembled on The monomolecular layer theory can be supplemented to analyze the effect of element La concentration on the tensile performances of BF/ERCs with the model shown in Figure 11. At low concentrations, few La3+ were absorbed onto the BFs surfaces. As shown in Figure 11a, the arrangement of La atoms on BFs surfaces was discontinuous with a lot of voids, resulting in the failure of BF/ERCs occurring firstly on the location without La atoms under external load. Thus, the discontinuous interface between BFs and the epoxy resin is insufficient to improve the mechanical performance of BF/ERCs obviously. When La element increased to the best concentration, 0.5 wt.%, the uniform and compact monomolecular layer on the BFs surfaces exhibits high adhesive strength between BFs and the matrix, as shown in Figure 11b. The mechanical performances of BF/ERCs reached to the highest value, including the tensile strength, the bending strength, and ILSS.

the BFs surfaces to form multimolecular layer, as shown in Figure 12. Under external load, failure of BF/ERCs firstly occurred on the interlayer of La atoms interlinked by weak Van der Waals force, resulting in the decreased performance of BF/ERCs. When La3+ concentration exceeded 0.5 wt.%, excessive La atoms were assembled on the BFs surfaces to form multimolecular layer, as shown in Figure 12. Under external load, failure of BF/ERCs firstly occurred on the interlayer of La atoms interlinked by weak Van der Waals force, resulting in the decreased performance of BF/ERCs.

**Figure 11.** Model of monomolecular layer theory. (**a**) the model with less La3+; (**b**) the model with

enough La3+; (**c**) the model with excess La3+.

containing La3+ 0.9 wt.%

der Waals force, resulting in the decreased performance of BF/ERCs.

highest value, including the tensile strength, the bending strength, and ILSS.

**Figure 10.** SEM images of fracture surfaces of BF/ERCs: (**a**) untreated; (**b**) treated with modification solution containing La3+ 0.1 wt.%; (**c**) treated with modification solution containing La3+ 0.3 wt.%; (**d**) treated with modification solution containing La3+ 0.5 wt.%; (**e**) treated with modification solution containing La3+ 0.7 wt.%; (**f**) treated with modification solution

> The monomolecular layer theory can be supplemented to analyze the effect of element La concentration on the tensile performances of BF/ERCs with the model shown in Figure 11. At low concentrations, few La3+ were absorbed onto the BFs surfaces. As shown in Figure 11a, the arrangement of La atoms on BFs surfaces was discontinuous with a lot of voids, resulting in the failure of BF/ERCs occurring firstly on the location without La atoms under external load. Thus, the discontinuous interface between BFs and the epoxy resin is insufficient to improve the mechanical performance of BF/ERCs obviously. When La element increased to the best concentration, 0.5 wt.%, the uniform and compact monomolecular layer on the BFs surfaces exhibits high adhesive strength between BFs and the matrix, as shown in Figure 11b. The mechanical performances of BF/ERCs reached to the

> When La3+ concentration exceeded 0.5 wt.%, excessive La atoms were assembled on the BFs surfaces to form multimolecular layer, as shown in Figure 12. Under external load, failure of BF/ERCs firstly occurred on the interlayer of La atoms interlinked by weak Van

**Figure 11.** Model of monomolecular layer theory. (**a**) the model with less La3+; (**b**) the model with enough La3+; (**c**) the model with excess La3+. **Figure 11.** Model of monomolecular layer theory. (**a**) the model with less La3+; (**b**) the model with enough La3+; (**c**) the model with excess La3+ .

**Figure 12.** La3+ attached onto BFs surfaces.

#### **4. Discussion**

**Figure 12.** La3+ attached onto BFs surfaces. *4.1. Analysis about Modification Mechanism of La3+*

**4. Discussion**  In Figures 1–5, the analysis based on the FT-IR spectra and the XPS results of BFs shows that, compared to untreated BFs, active oxygen-containing functional groups on the fiber surfaces increased, once BFs is treated with the rare earth modification solution. That was ascribed to the mechanism of La element in the modification solution as follows.

*4.1. Analysis about Modification Mechanism of La3+* In Figure 1 and Figures 2–5, the analysis based on the FT-IR spectra and the XPS results of BFs shows that, compared to untreated BFs, active oxygen-containing functional The rare earth elements with 4f electronic shell have good chemical activity. Once polarized, they have strong affinity to the nonmetal elements and turn into active elements in alcohol solution with the typical nonmetal elements such as C, H, O and N [26–28]. Consequently, with the results in Section 3.2.2., the coordination bonds between La ions and nonmetal elements are formed and La elements are attached onto the fiber surfaces, as shown in Figure 12.

groups on the fiber surfaces increased, once BFs is treated with the rare earth modification solution. That was ascribed to the mechanism of La element in the modification solution as follows. The rare earth elements with 4f electronic shell have good chemical activity. Once The coordination number of La element changes from 3 to 12, while the majority level remains 8. In this study, the rare earth modification solution was the alcohol solution with a variety of organic compounds, such as urea and citric acid, as shown in Figure 13a. As the active chemical cores, La ions attached on the BFs surfaces were combined with a lot of active organic groups in the solution to generate the multicomponent complex [26–28], shown in Figure 13b. With the active organic groups absorbed onto the fiber surfaces to form the macromolecular membrane, the chemical activity on the fiber surfaces could be improved obviously, as shown in Figure 13c. As seen in Figure 6, the La ions can also be

28]. Consequently, with the results in Section 3.2.2., the coordination bonds between La

ions and nonmetal elements are formed and La elements are attached onto the fiber sur-

remains 8. In this study, the rare earth modification solution was the alcohol solution with

a variety of organic compounds, such as urea and citric acid, as shown in Figure 13a. As

the active chemical cores, La ions attached on the BFs surfaces were combined with a lot

of active organic groups in the solution to generate the multicomponent complex [26–28],

shown in Figure13b. With the active organic groups absorbed onto the fiber surfaces to

form the macromolecular membrane, the chemical activity on the fiber surfaces could be

improved obviously, as shown in Figure 13c. As seen in Figure 6, the La ions can also be

embedded in the defect points on the BFs surfaces to generate more active chemical cores,

and hence the chemical activity of the fiber surfaces can be further improved.

The coordination number of La element changes from 3 to 12, while the majority level

faces, as shown in Figure 12.

embedded in the defect points on the BFs surfaces to generate more active chemical cores, and hence the chemical activity of the fiber surfaces can be further improved. embedded in the defect points on the BFs surfaces to generate more active chemical cores, and hence the chemical activity of the fiber surfaces can be further improved.

*Coatings* **2021**, *11*, 666 14 of 18

**Figure 12.** La3+ attached onto BFs surfaces.

La3+ +

C O

OH

COOH

*4.1. Analysis about Modification Mechanism of La3+*

:La3+

BF BF

O

O C

C O OH

H

La3+

In Figure 1 and Figures 2–5, the analysis based on the FT-IR spectra and the XPS

The rare earth elements with 4f electronic shell have good chemical activity. Once

The coordination number of La element changes from 3 to 12, while the majority level

remains 8. In this study, the rare earth modification solution was the alcohol solution with a variety of organic compounds, such as urea and citric acid, as shown in Figure 13a. As the active chemical cores, La ions attached on the BFs surfaces were combined with a lot of active organic groups in the solution to generate the multicomponent complex [26–28], shown in Figure13b. With the active organic groups absorbed onto the fiber surfaces to form the macromolecular membrane, the chemical activity on the fiber surfaces could be improved obviously, as shown in Figure 13c. As seen in Figure 6, the La ions can also be

results of BFs shows that, compared to untreated BFs, active oxygen-containing functional groups on the fiber surfaces increased, once BFs is treated with the rare earth modification solution. That was ascribed to the mechanism of La element in the modification solution

polarized, they have strong affinity to the nonmetal elements and turn into active elements in alcohol solution with the typical nonmetal elements such as C, H, O and N [26– 28]. Consequently, with the results in Section 3.2.2., the coordination bonds between La ions and nonmetal elements are formed and La elements are attached onto the fiber sur-

**4. Discussion** 

as follows.

faces, as shown in Figure 12.

**Figure 13.** The chemical reaction mechanism of the La3+ modification solution: (**a**) the molecular formula of urea and citric acid in the modification solution; (**b**) the chemical combination between La3+ and the active groups in the modification solution; (**c**) the chemical combination between the **Figure 13.** The chemical reaction mechanism of the La3+ modification solution: (**a**) the molecular formula of urea and citric acid in the modification solution; (**b**) the chemical combination between La3+ and the active groups in the modification solution; (**c**) the chemical combination between the BFs and the modification to introduce the more active groups.

BFs and the modification to introduce the more active groups. However, the abundant active groups introduced by the excess La3+ were aggerated on the fibers' surfaces to be supersaturated, resulting in the break of the macromolecular membrane and loss of active groups, as shown in Figure 4e,f. Meanwhile, with the excess La3+, the generated Si–OH between SiO2 of the fibers' surface and the modification solu-However, the abundant active groups introduced by the excess La3+ were aggerated on the fibers' surfaces to be supersaturated, resulting in the break of the macromolecular membrane and loss of active groups, as shown in Figure 4e,f. Meanwhile, with the excess La3+, the generated Si–OH between SiO<sup>2</sup> of the fibers' surface and the modification solution under hydrolytic action restrain the further hydrolytic action of SiO2, leading to the decrease of Si–OH and Si–O–Si in Figure 4e,f, which further reduced the surface activity of fibers. Thus, the La3+ concentration of 0.5% was the most suitable.

tion under hydrolytic action restrain the further hydrolytic action of SiO2, leading to the decrease of Si–OH and Si–O–Si in Figure 4e,f, which further reduced the surface activity

*4.2. Analysis of Enhancement Mechanism of BFs/ECR's Mechanical Property Modified with La3+*

epoxy resin with ali-phatic polyamine curing agent took place and generated two oxhy-

**Figure 14.** The crosslinking reaction of epoxy resin with aliphatic polyamine curing agent

well as the tensile strength, the bending strength, and ILSS.

proved, as well as the mechanical performances of BF/ERCs.

In the process of the resin matrix synthesis, the following crosslinking reaction of

Based on the FT-IR spectra and the XPS results of BFs, the active functional groups

However, parts of La ions, which were absorbed on the modified BFs surfaces, did

not take part in the coordination bond with active groups. When the modified BFs were put into the epoxy resin, these La ions can be combined with oxhydryl generated in the above crosslinking reaction, because of the typical chemical activities and the variable coordination number of La3+. As shown in Figure 15b, under the effect of the formed coordination bond, the adhesion strength between BFs and epoxy matrix was further im-

increased on the surface of BFs treated with the rare earth modification solution. With the oxhydryl generated in the above crosslinking reaction, the active functional groups took part in the dehydration condensation reaction, when BFs were in sufficient contact with epoxy resin. The bonding of BFs and epoxy resin was based on the chemical bonds, such as the ester group and the ether bond, so that the bonding force improved significantly, as shown in Figure 15a. Thus, when La3+ concentration was 0.5 wt.%, the absorbed active groups reached to the maximumand the bonding force was correspondingly highest, as

dryl groups, as shown in Figure 14.

*4.2. Analysis of Enhancement Mechanism of BFs/ECR's Mechanical Property Modified with La3+ 4.2. Analysis of Enhancement Mechanism of BFs/ECR's Mechanical Property Modified with La3+*

**Figure 13.** The chemical reaction mechanism of the La3+ modification solution: (**a**) the molecular formula of urea and citric acid in the modification solution; (**b**) the chemical combination between La3+ and the active groups in the modification solution; (**c**) the chemical combination between the

However, the abundant active groups introduced by the excess La3+ were aggerated on the fibers' surfaces to be supersaturated, resulting in the break of the macromolecular membrane and loss of active groups, as shown in Figure 4e,f. Meanwhile, with the excess La3+, the generated Si–OH between SiO2 of the fibers' surface and the modification solution under hydrolytic action restrain the further hydrolytic action of SiO2, leading to the decrease of Si–OH and Si–O–Si in Figure 4e,f, which further reduced the surface activity

In the process of the resin matrix synthesis, the following crosslinking reaction of epoxy resin with ali-phatic polyamine curing agent took place and generated two oxhydryl groups, as shown in Figure 14. In the process of the resin matrix synthesis, the following crosslinking reaction of epoxy resin with ali-phatic polyamine curing agent took place and generated two oxhydryl groups, as shown in Figure 14.

of fibers. Thus, the La3+ concentration of 0.5% was the most suitable.

BFs and the modification to introduce the more active groups.

*Coatings* **2021**, *11*, 666 15 of 18

**Figure 14.** The crosslinking reaction of epoxy resin with aliphatic polyamine curing agent **Figure 14.** The crosslinking reaction of epoxy resin with aliphatic polyamine curing agent.

Based on the FT-IR spectra and the XPS results of BFs, the active functional groups increased on the surface of BFs treated with the rare earth modification solution. With the oxhydryl generated in the above crosslinking reaction, the active functional groups took part in the dehydration condensation reaction, when BFs were in sufficient contact with epoxy resin. The bonding of BFs and epoxy resin was based on the chemical bonds, such as the ester group and the ether bond, so that the bonding force improved significantly, as shown in Figure 15a. Thus, when La3+ concentration was 0.5 wt.%, the absorbed active groups reached to the maximumand the bonding force was correspondingly highest, as well as the tensile strength, the bending strength, and ILSS. Based on the FT-IR spectra and the XPS results of BFs, the active functional groups increased on the surface of BFs treated with the rare earth modification solution. With the oxhydryl generated in the above crosslinking reaction, the active functional groups took part in the dehydration condensation reaction, when BFs were in sufficient contact with epoxy resin. The bonding of BFs and epoxy resin was based on the chemical bonds, such as the ester group and the ether bond, so that the bonding force improved significantly, as shown in Figure 15a. Thus, when La3+ concentration was 0.5 wt.%, the absorbed active groups reached to the maximumand the bonding force was correspondingly highest, as well as the tensile strength, the bending strength, and ILSS. *Coatings* **2021**, *11*, 666 16 of 18

However, parts of La ions, which were absorbed on the modified BFs surfaces, did

**Figure 15.** Effect of La3+ on the interface of BFs and epoxy resin. (**a**)the chemical reaction between the absorbed active groups and the epoxy resin containing curing agent; (**b**) the coordination reaction between La3+ and the epoxy resin containing curing agent **Figure 15.** Effect of La3+ on the interface of BFs and epoxy resin. (**a**) the chemical reaction between the absorbed active groups and the epoxy resin containing curing agent; (**b**) the coordination reaction between La3+ and the epoxy resin containing curing agent.

**5. Conclusions**  In this research, the modification of basalt fibers with the modification solution of different La3+ concentrations was carried out. Moreover, the effect of modification with different La3+ concentrations and the mechanical properties for basalt fiber/epoxy resin composites modified with La3+ were evaluated. However, parts of La ions, which were absorbed on the modified BFs surfaces, did not take part in the coordination bond with active groups. When the modified BFs were put into the epoxy resin, these La ions can be combined with oxhydryl generated in the above crosslinking reaction, because of the typical chemical activities and the variable coordination number of La3+. As shown in Figure 15b, under the effect of the formed coordination bond, the adhesion strength between BFs and epoxy matrix was further improved, as well as the mechanical performances of BF/ERCs.

The study about the chemical composition, the functional groups and the morphol-

In addition, the modification mechanism of La3+ and enhancement mechanism of

BFs/ECR's mechanical property modified with La3+ were stated with the strong affinity of La to the nonmetal elements, indicating that the modification of BFs with La3+ was effec-

**Author Contributions:** Conceptualization, C.L.; methodology, C.L.; software, H.W.; validation, C.L., X.H., and Y.F.; formal analysis, C.L.; investigation, C.L., H.W., and Y.S.; resources, C.L.; data curation, Y.S.; writing—original draft preparation, C.L. and H.W.; writing—review and editing, C.L. and H.W.; visualization, H.W.; supervision, C.L.; project administration, C.L.; funding acquisition,

**Funding:** The research was funded by Science Foundation of the National Key Laboratory of Science and Technology on Advanced Composites in Special Environment (Grand No. JCKYS2019603C006).

tive and the mechanical property of the prepared BFs/ECR composites was excellent.

C.L. All authors have read and agreed to the published version of the manuscript.

**Institutional Review Board Statement:** Not applicable.

**Informed Consent Statement:** Not applicable.

several analytical techniques (FTIR, XPS, and SEM), confirmed that La element in the rare earth modification solution could link active oxygen-containing functional groups to the BFs surfaces to improve the roughness and the activity of the fiber surfaces. When the La3+ concentration in the rare earth modification solution was 0.5 wt.%, the activity of BFs' surface reached the strongest with the most introduced active groups. It is also determined that the mechanical performances of BF/ERCs, including the tensile strength, the bending strength and ILSS, could be significantly enhanced by the modified BFs due to the formed chemical reaction between resin matrix and the more active groups introduced by La3+. With the La3+ concentration in the rare earth modification solution reaching 0.5 wt.%, the bonding between the resin matrix and BFs is demonstrated to be the best and the tensile strength, the bending strength and ILSS were up to 458.7, 556.7 and 16.77 Mpa, and improved by 56.22%, 103.32% and 88% compared with those of the unmodified ones, re-

spectively.

#### **5. Conclusions**

In this research, the modification of basalt fibers with the modification solution of different La3+ concentrations was carried out. Moreover, the effect of modification with different La3+ concentrations and the mechanical properties for basalt fiber/epoxy resin composites modified with La3+ were evaluated.

The study about the chemical composition, the functional groups and the morphology of untreated and treated BFs' surface with the rare earth modification solution using several analytical techniques (FTIR, XPS, and SEM), confirmed that La element in the rare earth modification solution could link active oxygen-containing functional groups to the BFs surfaces to improve the roughness and the activity of the fiber surfaces. When the La3+ concentration in the rare earth modification solution was 0.5 wt.%, the activity of BFs' surface reached the strongest with the most introduced active groups. It is also determined that the mechanical performances of BF/ERCs, including the tensile strength, the bending strength and ILSS, could be significantly enhanced by the modified BFs due to the formed chemical reaction between resin matrix and the more active groups introduced by La3+ . With the La3+ concentration in the rare earth modification solution reaching 0.5 wt.%, the bonding between the resin matrix and BFs is demonstrated to be the best and the tensile strength, the bending strength and ILSS were up to 458.7, 556.7 and 16.77 Mpa, and improved by 56.22%, 103.32% and 88% compared with those of the unmodified ones, respectively.

In addition, the modification mechanism of La3+ and enhancement mechanism of BFs/ECR's mechanical property modified with La3+ were stated with the strong affinity of La to the nonmetal elements, indicating that the modification of BFs with La3+ was effective and the mechanical property of the prepared BFs/ECR composites was excellent.

**Author Contributions:** Conceptualization, C.L.; methodology, C.L.; software, H.W.; validation, C.L., X.H. and Y.F.; formal analysis, C.L.; investigation, C.L., H.W. and Y.S.; resources, C.L.; data curation, Y.S.; writing—original draft preparation, C.L. and H.W.; writing—review and editing, C.L., H.W. and X.Z.; visualization, H.W. and X.Z.; supervision, C.L.; project administration, C.L.; funding acquisition, C.L. All authors have read and agreed to the published version of the manuscript.

**Funding:** The research was funded by Science Foundation of the National Key Laboratory of Science and Technology on Advanced Composites in Special Environment (Grand No. JCKYS2019603C006).

**Institutional Review Board Statement:** Not applicable.

**Informed Consent Statement:** Not applicable.

**Data Availability Statement:** The data presented in this study are available on request from the corresponding author. The data are not publicly available as the data also form part of an ongoing study.

**Conflicts of Interest:** The authors declare no conflict of interest.

#### **References**

