# Heat Treatment Effects on the Mechanical Properties and Morphologies of Poly (Lactic Acid)/Poly (Butylene Adipate-co-terephthalate) Blends

Authors: Hsien-Tang Chiu; Szu-Yuan Huang; Yan-Fu Chen; Ming-Tai Kuo; Tzong-Yiing Chiang; Chi-Yung Chang; Yu-Hsiang Wang
Journal: International Journal of Polymer Science
 (2013)

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## Abstract

In this study the relationships between mechanicals properties and morphology of the poly (lactic acid) (PLA)/poly (butylene adipate-co-terephthalate) (PBAT) blends with or without heat treatment were investigated. The differential scanning calorimetry (DSC) analysis showed that blends have a two-phase structure indicating that they are immiscible. On the other hand, the PLA/PBAT (30/70) blend achieved the best tensile and impact strength because of its sea-island morphology, except for high PBAT content. The PLA/PBAT (70/30) and PLA/PBAT (50/50) blends showed irregular and directive-layer morphologies, in scanning electron microscopy (SEM) analysis, producing a break cross-section with various fiber shapes. Both blends showed lower tensile strength and impact strength than the PLA/PBAT (30/70). After heat treatment, the PLA/PBAT blends showed high modulus of tensile and HDT because of a high degree of crystallization. The high degree of crystallization in the blends, which originated in the heat treatment, reduced their impact strength and elongation. However, the effect of high degree of crystallization on the PLA/PBAT (30/70) blend was small because of its sea-island morphology.


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## Body

## 1. Introduction

The large-scale production and consumption of plastics has created several problems: diminishing oil resources, increased discharge of CO2 into the atmosphere, and environmental pollution caused by waste plastics. However, the development and acceptance of biodegradable polymers might be a solution to the waste plastics problem.Polylactic aced (PLA) is a biodegradable thermal plastic that can be manufactured from biomass materials, such as cornstarch or beet sugar [1–3]. Although PLA has excellent biodegradability and tensile strength, its elongation ability, impact strength, shock absorbance, toughness, physical aging, and heat deflection properties are unsatisfactory for practical applications [4, 5]. Therefore, many researchers have attempted to increase the toughness, rigidity, and biodegradability of PLA by blending it with various biodegradable soft polymers, including poly (propylene carbonate) (PCC) [3], poly (butylene succinate adipate) (PBSA) [4], poly (butylene adipate-co-terephthalate) (PBAT) [5], and poly (amide elastomer) (PAE) [6]. To improve the heat distortion temperature of PLA, it can be dispersed with nanomontmorillonite or melt-blended with high-temperature-resistant engineering plastics [7, 8]. However, the resulting improvement in toughness remains far less than that of soft polymers.In recent years, much attention has increased on poly (lactic acid) (PLA) with poly (butylene adipate-co-butylene terephthalate) (PBAT) blend system [9–13] due to elastomeric property of the PBAT complements brittleness of the PLA. PBAT is a fully biodegradable, flexible aliphatic-aromatic copolyester designed for film extrusion and extrusion coating. Its most attractive feature is its high elongation at break [5]. Several studies [5, 11, 12] showed that the elongation and toughness of PLA/PBAT blends were dramatically increased although their thermal behavior presented a two-phase structure and was immiscible. The SEM micrographs showed that the toughening mechanism of PLA/PBAT blends was from brittle fracture of the PLA to ductile fracture of the blends. Therefore, the immiscible polymer blends and  their morphologies have important effects on mechanical properties. The studies above focused on low PBAT contents. Li  et al. [13] have investigated the PLA/PBAT blends with high PBAT contents, but they devoted their study to relationships between rheological properties and morphology of the blends.On the other hand, the heat deflection of the resulting PLA-based materials requires further improvement for practical applications. Compared to the general crystalline polymer polypropylene (PP), PLA has a similar Tm value but a much higher glass transition temperature (Tg). However, PLA has a much lower heat deflection than PP. The main reason for this phenomenon is that although PLA is a crystalline polymer, almost no crystallization occurs during the molding process in practice, as evidenced from its thermal behavior during differential scanning calorimetry (DSC) [5, 10].As mentioned, few studies have investigated the improvement of PLA-based HDT and the relationships between mechanicals properties and morphology for the PLA/PBAT blends. Therefore, the objectives of the present work are to blend PLA with PBAT using a melt-blending method in a twin-screw extruder. The various PLA/PBAT blends were prepared by injection molding. The PLA/PBAT blends were annealed at 100°C for 8 h and 24 h investigate the effects of crystallization on their tensile strength, impact strength, and heat deflection. We tested the tensile strength, Izod impact strength, DSC, SEM, XRD, and HDT to investigate the relationships between the morphology and mechanical properties of the PLA/PBAT blends. This study also presents a discussion of the effects of various heat treatment conditions on mechanical properties.


## 2. Experimental

### 2.1. Materials and Samples Preparation

The PLA (polymer 2100D) and PBAT (ECOFLEX 7011) polymers used in this study were obtained from NatureWorks and BASF, respectively. The PLA and PBAT pellets were dried in a vacuum oven at 80°C for 8 h prior to use and subsequently melt-blended in a twin-screw extruder operating at a mixing speed of 600 rpm at 150–160°C. The PLA/PBAT weight ratios were 100/0, 70/30, 50/50, 30/70, and 0/100. After blending, all of the samples were cooled to room temperature in an air atmosphere. Samples of the blends were molded at 180°C using an injection-molding instrument (SPC-303BL Type, Yeun Chenn), with process times of approximately 100 s (injection), 20 s (forming), and 260 s (cooling). The processes were performed at a mold temperature of 40°C.


### 2.2. Measurements

#### 2.2.1. DSC

The DSC analysis in this study was conducted using a Perkin-Elmer DSC-PYRIS-1 instrument equipped with an ice-water and liquid nitrogen cooler. Indium was used to calibrate the temperature and the heat of fusion. The amount of sample used for the measurements was approximately 4–7 mg. The initial scan of the specimens proceeded from 40 to 200°C at a rate of 10°C/min under a N2 atmosphere. The melt-quenched scans of the specimens were similar to their initial scans. The specimens were heated to 200°C and held at that temperature for 1 min to erase their thermal history. They were then cooled to 40°C at a rate of 100°C/min. The thermograms of the specimens were subsequently obtained by heating at a rate of 10°C/min from 40 to 200°C. All of the samples were annealed in an oven at 100°C for 8 and 24 h after injection molding. The thermograms of the samples from 40 to 200°C were then obtained at a heating rate of 10°C/min.


#### 2.2.2. Wide-Angle X-Ray Diffraction (WAXD)

Samples were analyzed using a Shimadzu XRD-6000 WAXD apparatus and Cu Kα radiation (λ=0.154 nm) under a voltage of 40 kV and a current of 100 mA. Diffraction intensities were counted in 0.05° steps at a scanning speed of 5°/min. The spectra were recorded in an angular 2θ range from 10 to 40°  at room temperature.


#### 2.2.3. Tensile Strength

The tensile strengths of the blends were evaluated using a tensile-testing machine (MTS Qtest-5) and material-testing software (Test Work 4). The tensile strength tests were performed at 25°C with a cross-head speed of 100 mm/min and a 5 kN load cell.


#### 2.2.4. Impact Test

Impact tests were performed at room temperature using an Izod Impact testing machine with a pendulum weight of 1.377 kgf, a pendulum angle of 150°, and a distance from the pendulum head of 32.83 cm.


#### 2.2.5. Heat Deflection Temperature (HDT)

The HDT tests in this study were performed using a GOTECH HV-2000 A HDT testing machine operating at a heating rate of 2°C/min and a load of 66 psi.


## 2.1. Materials and Samples Preparation

The PLA (polymer 2100D) and PBAT (ECOFLEX 7011) polymers used in this study were obtained from NatureWorks and BASF, respectively. The PLA and PBAT pellets were dried in a vacuum oven at 80°C for 8 h prior to use and subsequently melt-blended in a twin-screw extruder operating at a mixing speed of 600 rpm at 150–160°C. The PLA/PBAT weight ratios were 100/0, 70/30, 50/50, 30/70, and 0/100. After blending, all of the samples were cooled to room temperature in an air atmosphere. Samples of the blends were molded at 180°C using an injection-molding instrument (SPC-303BL Type, Yeun Chenn), with process times of approximately 100 s (injection), 20 s (forming), and 260 s (cooling). The processes were performed at a mold temperature of 40°C.


## 2.2. Measurements

### 2.2.1. DSC

The DSC analysis in this study was conducted using a Perkin-Elmer DSC-PYRIS-1 instrument equipped with an ice-water and liquid nitrogen cooler. Indium was used to calibrate the temperature and the heat of fusion. The amount of sample used for the measurements was approximately 4–7 mg. The initial scan of the specimens proceeded from 40 to 200°C at a rate of 10°C/min under a N2 atmosphere. The melt-quenched scans of the specimens were similar to their initial scans. The specimens were heated to 200°C and held at that temperature for 1 min to erase their thermal history. They were then cooled to 40°C at a rate of 100°C/min. The thermograms of the specimens were subsequently obtained by heating at a rate of 10°C/min from 40 to 200°C. All of the samples were annealed in an oven at 100°C for 8 and 24 h after injection molding. The thermograms of the samples from 40 to 200°C were then obtained at a heating rate of 10°C/min.


### 2.2.2. Wide-Angle X-Ray Diffraction (WAXD)

Samples were analyzed using a Shimadzu XRD-6000 WAXD apparatus and Cu Kα radiation (λ=0.154 nm) under a voltage of 40 kV and a current of 100 mA. Diffraction intensities were counted in 0.05° steps at a scanning speed of 5°/min. The spectra were recorded in an angular 2θ range from 10 to 40°  at room temperature.


### 2.2.3. Tensile Strength

The tensile strengths of the blends were evaluated using a tensile-testing machine (MTS Qtest-5) and material-testing software (Test Work 4). The tensile strength tests were performed at 25°C with a cross-head speed of 100 mm/min and a 5 kN load cell.


### 2.2.4. Impact Test

Impact tests were performed at room temperature using an Izod Impact testing machine with a pendulum weight of 1.377 kgf, a pendulum angle of 150°, and a distance from the pendulum head of 32.83 cm.


### 2.2.5. Heat Deflection Temperature (HDT)

The HDT tests in this study were performed using a GOTECH HV-2000 A HDT testing machine operating at a heating rate of 2°C/min and a load of 66 psi.


## 2.2.1. DSC

The DSC analysis in this study was conducted using a Perkin-Elmer DSC-PYRIS-1 instrument equipped with an ice-water and liquid nitrogen cooler. Indium was used to calibrate the temperature and the heat of fusion. The amount of sample used for the measurements was approximately 4–7 mg. The initial scan of the specimens proceeded from 40 to 200°C at a rate of 10°C/min under a N2 atmosphere. The melt-quenched scans of the specimens were similar to their initial scans. The specimens were heated to 200°C and held at that temperature for 1 min to erase their thermal history. They were then cooled to 40°C at a rate of 100°C/min. The thermograms of the specimens were subsequently obtained by heating at a rate of 10°C/min from 40 to 200°C. All of the samples were annealed in an oven at 100°C for 8 and 24 h after injection molding. The thermograms of the samples from 40 to 200°C were then obtained at a heating rate of 10°C/min.


## 2.2.2. Wide-Angle X-Ray Diffraction (WAXD)

Samples were analyzed using a Shimadzu XRD-6000 WAXD apparatus and Cu Kα radiation (λ=0.154 nm) under a voltage of 40 kV and a current of 100 mA. Diffraction intensities were counted in 0.05° steps at a scanning speed of 5°/min. The spectra were recorded in an angular 2θ range from 10 to 40°  at room temperature.


## 2.2.3. Tensile Strength

The tensile strengths of the blends were evaluated using a tensile-testing machine (MTS Qtest-5) and material-testing software (Test Work 4). The tensile strength tests were performed at 25°C with a cross-head speed of 100 mm/min and a 5 kN load cell.


## 2.2.4. Impact Test

Impact tests were performed at room temperature using an Izod Impact testing machine with a pendulum weight of 1.377 kgf, a pendulum angle of 150°, and a distance from the pendulum head of 32.83 cm.


## 2.2.5. Heat Deflection Temperature (HDT)

The HDT tests in this study were performed using a GOTECH HV-2000 A HDT testing machine operating at a heating rate of 2°C/min and a load of 66 psi.


## 3. Results and Discussion

### 3.1. Phase Transition Regions and Miscibility

Semicrystalline polymers possess amorphous and crystalline phases, each of which has at least a phase transition region, that is, a glass transition temperature (Tg) and a melting temperature (Tm). The phase transition regions can be determined by DSC analysis, revealing the miscibility of polymer blends. A miscible polymer blend is homogeneous and usually displays a single Tg between those of the pure components, whereas a compatible blend shows both Tgs although these eventually shift toward one another.The thermograms of all samples in the initial and melt-quenched scans have several endothermic regions (Figures1 and 2). Table 1 lists the characteristic temperatures of glass transition regions for all samples. The glass transition temperatures (Tg) in this study were determined by the half-heat capacity (1/2  Cp) in the glass transition region. The PLA in the initial and melt-quenched DSC thermograms showed a Tg and Tm of 60°C and 165°C, respectively, whereas the PBAT displayed  Tg and Tm of approximately −33°C and 112°C, respectively (Tables 2 and 3). This result shows that PLA and PBAT are biodegradable crystalline plastics with amorphous and crystalline phases. The PBAT has a lower Tg broader Tm region than PLA (Figures 1 and 2) and provides good softness and impact resistance.Table 1
Characteristic temperatures of phase transition and enthalpy values of PLA/PBAT blends in the initial scan of DSC.
Code
T
g
-PBAT
1
T
g
-PLA
2
Δ
T
g
3
Δ
H
cc
4 (J/g)
T
m
-PLA
5 (°C)
Δ
H
m
-PLA
5 (J/g)
PLA
—
60.7
—
-
17.39
164.1
37
PLA/PBAT (70/30)
-
32.1
59.7
91.8
-
13.71
164.3
22.38
PLA/PBAT (50/50)
-
32.8
59.2
91.0
-
7.39
163.9
16.58
PLA/PBAT (30/70)
-
30.9
57.6
88.5
-
3.61
163.7
9.91
PBAT
−34
—
—
1
T
g
-PBAT: The temperature of glass transition region of PBAT.
2
T
g
-PLA: The temperature of glass transition region of PLA.
3
Δ
T
g: ΔTg=Tg-PLA-Tg-PBAT.
4
Δ
H
cc: The exothermal enthalpy of PLA cold-crystallization (re-crystallization).
5
T
m
-PLA  and ΔHm-PLA: The melting temperature and crystal melting enthalpy of PLA.Table 2
Characteristic temperatures of phase transition and enthalpy values of PLA/PBAT blends in the melt-quenched scan of DSC.
Code
T
g
-PBAT
1
T
g
-PLA
2
Δ
T
g
3
Δ
H
cc
4 (J/g)
T
m
-PLA
5 (°C)
Δ
H
m
-PLA
5 (J/g)
PLA
—
59.2
—
-
21.31
164.3
37.2
PLA/PBAT (70/30)
-
33.6
60.1
93.4
-
17.59
164.9
22.29
PLA/PBAT (50/50)
-
32.9
59.5
92.4
-
10.41
165.3
14.36
PLA/PBAT (30/70)
-
30.1
57.2
87.3
-
6.84
165.2
9.65
PBAT
−35.1
—
—
—
—
—
1
T
g
-PBAT: The temperature of glass transition region of PBAT.
2
T
g
-PLA: The temperature of glass transition region of PLA.
3
Δ
T
g: ΔTg=Tg-PLA-Tg-PBAT.
4
Δ
H
cc: The exothermal enthalpy of PLA cold-crystallization (re-crystallization).
5
T
m
-PLA and ΔHm-PLA: The melting temperature and crystal melting enthalpy of PLA.Table 3
The enthalpy and crystallinity of PLA/PBAT blends treated at 100°C for 8 and 24 hr.
Code
0 hr
8 hr
24 hr
Δ
H
m
a (J/g)
X
c
b  (%)
Δ
H
m
a (J/g)
X
c
b (%)
Δ
H
m
a (J/g)
X
c
b (%)
PLA
37
42.44
39.47
43.44
31.59
34
PLA/PBAT (70/30)
22.38
32.3
24.03
33.3
21.23
32.61
PLA/PBAT (50/50)
16.58
33.72
16.32
35.1
15.68
33.72
PLA/PBAT (30/70)
9.91
34.62
9.66
34.62
9.14
32.76
a
Δ
H
m: The crystal melting enthalpy of PLA.
b
X
c: The degree of crystallinity (Xc) of PLA.Figure 1
Initial scanning DSC thermogram of PLA/PBAT blends.Figure 2
Melt-quenched scanning DSC thermogram of PLA/PBAT blends.


#### 3.1.1. Glass Transition Region of Blends

The PLA/PBAT blends in the initial and melt-quenched scan exhibit 2 glass transition regions at approximately −35 to −30°C and 57 to 61°C. These regions are, respectively, associated with PBAT and PLATg  (Tg-PBAT and Tg-PLA) regions (Figures 1 and 2). The PLA/PBAT blends exhibit two Tg  regions, indicating that the blends are immiscible and present a two-phase structure. However, the Tg-PBAT and Tg-PLA values for various PLA/PBAT blends in the initial and melt-quenched scans changed in a small region at approximately −30 to −35°C and 57 to 61°C, respectively (Tables 1 and 2). Accordingly, the PLA and PBAT in the PLA/PBAT blends present a low compatibility. The ΔTg (Tg-PLA–Tg-PBAT) represents the degree of compatibility, which is affected by its morphology. The PLA/PBAT (30/70) has the lowest ΔTg value, and the ΔTg values for both PLA/PBAT (70/30) and PLA/PBAT (50/50) are relatively similar (Tables 1 and 2). This result indicates that the blends have at least two morphologies. The following SEM analysis presents the phase-separation structure and morphologies of these samples.The PLA/PBAT blends that underwent the melt-quenched process determine the compatibility of the blends and their phase-separation behavior. TheTg values (Tg-PBAT and Tg-PLA) under the melt-quenched scan for PLA and PBAT appeared to decrease slightly, and their Tg regions were broader than the initial scan (Table 1 and Figures 1 and 2). This result indicates that the amorphousness of PBAT and PLA increased under the melt-quenched process. The Tg regions in PLA/PBAT blends after the melt-quenched scan also show two Tg regions associated with the PBAT and PLA Tg regions, respectively. The ΔTg, Tg-PBAT, and Tg-PLA values for PLA/PBAT blends after the melt-quenched process have exhibited a slight variation within the region of 2°C (Tables 1 and 2). Therefore, the morphologies of the blends are two-phase structures, and the compatibility of blends is low because the Tg values have no obvious variation after the melt quenching process. Spinodal decomposition (SD) is a mechanism for the rapid unmixing of a mixture of liquids or solids from one thermodynamic phase to form two coexisting phases during rapid cooling process [14]. The two-phase separation of PLA/PBAT blends is due to SD during proceeding in the quenching process [15]. The morphology of PLA/PBAT (30/70) structure after the quenching process was presented by a polarized optical microscope (POM) (Figure 11). It can be seen that PLA/PBAT blends exhibited the irregularly interwoven phase. As reported previously, SD typically yields an interwoven structure [16]. Thus, it might be implied that the morphology of PLA/PBAT was attributed to SD in the quenching process. The thermograms of Tg region for PLA at approximately 63°C show a melt-like peak, which disappears under melt-quenched scanning (Figures 1 and 2). This result suggests an enthalpy relaxation resulting from physical aging of PLA amorphous macromolecular chains [17]. This aging process involves certain local density changes of the amorphous phase, generating nuclei and facilitating the crystallization of PLA [18].


#### 3.1.2. Melting Transition Region

The crystal-melting temperature of PLA (Tm-PLA) in the initial scan presented melting at approximately 164°C, but the PBAT had no obvious melting endothermic region (Figure 1). The PLA/PBAT blends in the initial scanning displayed a crystal-melting endothermic region at approximately 164°C, and the enthalpy values in the initial scanning for the PLA/PBAT blends increased almost linearly as the PLA content increased (Table 2). Accordingly, the melting endothermic region of PLA/PBAT blends is associated with PLA crystallization. The melting-temperature (Tm-PLA) regions of the PLA and PLA/PBAT blends after melt-quenched scanning remained at approximately 164°C, and their crystal-melting enthalpy (ΔHm) values showed no obvious change (Tables 1 and 2). The uniform ΔHm values before and after melted-quenched scanning (Tables 1 and 2) indicate that the PLA in the PLA/PBAT blends has a high rate of crystallization or high crystallization ability. These results illustrate a high degree of phase separation for the PLA/PBAT because the crystallization ability does not change significantly under the melt quenching process. Therefore, the PLA and PBAT in the blends tend to form independent phases. The PLA and PLA/PBAT blends in the DSC curves at approximately 80–100°C under the initial and melt-quenched scans exhibit that an exothermal peak is associated with PLA recrystallization (cold crystallization). This is because the PLA in all samples has the only crystallization ability. This PLA recrystallization likely results from the cold crystallization processes of PLA because the cold crystallization only presents a polymer with a high crystallization ability. The region of the cold crystallization temperature and the enthalpies (ΔHcc) of crystal exothermal peak were almost uniform under the initial and melt-quenched scanning (Tables 1 and 2), indicating that the PBAT composition in the blends hardly affects the crystallization ability of PLA. Thus, the PLA and PBAT in the PLA/PBAT blends tend to form independent phase. Accordingly, the PLA/PBAT blends should exhibit a two-phase structure, as further verified in SEM analysis.To further investigate the crystalline characteristics of PLA/PBAT blends, all samples were annealed at 100°C for 8 and 24 h and were analyzed using DSC and WAXD. Figure3 shows that the melting temperatures of PLA/PBAT blends remained at approximately 164°C, indicating that their crystalline form remained unchanged by the annealing process. However, the enthalpy of melting crystal (ΔHm) and degree of crystallization (Xc) for the PLA/PBAT blends increased after annealing (Table 4). The ΔHm and Xc reached their maximum values after annealing at 100°C for 8 h and underwent thermal aging when annealed for longer times (24 h) as observed from the drop in crystallinity values. This increase in the ΔHm and Xc values might result from the high-oriented amorphous PLA macromolecular chains, which can easily incorporate the PLA crystalline lattice. Therefore, the PLA macromolecular chains with a high orientation recrystallize (cool-crystallize) at 80–100°C (Figures 1 and 3). The cool-crystalline structure disappeared after the annealing process (Figure 3), but Hm and Xc increased (Tables 1 and 2). These results verify that the macromolecular chains of high orientation merged with the raw crystals during the annealing process.Table 4
The impact strength (KJ/m) for all samples under the melt-quenching and various annealing.
Melt-quenching
Annealing at 100°C for 24 h
Annealing at 100°C for 8 h
Break after Izod impact Testing1
PLA
3.85
3.85
3.62
○
PLA/PBAT (70/30)
19.03
13.65
12.11
○
PLA/PBAT (50/50)
18.77
7.57
7.01
○
PLA/PBAT (30/70)
33.56
21.6
22.58
×
PBAT
30.5
30.75
29.24
×
○: Fracture.
×: Has not destroy.
1The extent of damage of sample after Izod impact testing.Figure 3
PLA/PBAT blends DSC annealing at 100°C for 8 hr.We also investigated the characteristics of the crystals and effects of annealing on the PBAT/PLA blends using WAXD (Figures4 and 5). Figure 4 shows that the WAXD curves for the untreated PLA present a strong diffraction peaks at 2θ=18.7° corresponding to the (203) crystal plane  [10]. The WAXD peaks for the untreated PLA/PBAT blends were almost the same as those for PLA, but the diffractive intensities of blends are lower than those of the PLA because of a low PLA content. Several small diffraction peaks appeared in all samples and might be associated with PLA microcrystallinity (Figure 4). The WAXD peaks of PLA and PLA/PBAT blends annealed for 8 h at 100°C exhibited strong diffraction peaks at 2θ=17.5°, except for 2θ=18.7°  (Figure 5). The maximum value of diffractive intensity for the PLA/PBAT blends in all diffraction peaks appears at 2θ = 17.5°  corresponding to the (200/110) crystal plane [10]. This result indicates that the PLA composition in the PLA/PBAT blends under the annealing process exhibits an orientation crystalline structure that originates in the amorphous PLA macromolecular chains of high orientation. The orientation of macromolecular chains in the study is caused by the shearing force under the mixed and injection-molding process. Accordingly, the ΔHm and Xc values of the PLA/PBAT blends annealed for 8 h and 24 h are higher than those  for untreated samples (Table 3). The ΔHm and Xc values of the PLA and PLA/PBAT blends annealed at 100°C for 24 h are slightly lower than those of samples annealed for 8 h (Table 3), verifying that the PLA crystal undergoes thermal aging when annealed at 100°C for 24 h. The amorphous PLA macromolecular chains of high orientation verify the effects of cool crystallization on the initial and melt-quenched DSC scanning. We use the PLA that is an extrusion grade plastic with a low crystallinity. Thus, although the DSC heating thermograms of the PLA did not show melting endothermal peak, its DSC cooling thermograms displayed a broad weak melting exothermal peak in the temperature range of 105–45°C (Figure 1(b)).Figure 4
WAXD patterns of the untreated P LA/PBAT blends.Figure 5
WAXD patterns of PLA/PBAT blends annealing at 100°C for 8 hrs.


### 3.2. Mechanical Properties and Morphologies

As mentioned in the DSC and WAXD analyses, the PLA in the blends was a semicrystalline polymer with a high crystallization ability. Conversely, the PBAT presented features of an amorphous polymer. The PLA/PBAT blends had two-phase structure. The compatibility and morphology of the blends, which are associated with their components, determine the mechanical properties such as tensile and impact strength. This section presents the relationships between mechanical properties and morphologies as revealed by tensile strength and impact strength tests.


#### 3.2.1. Tensile Strength

Figure6(a) shows the stress-strain curves of all untreated samples at room temperature. PLA has a high stress and high initial modulus, but its strain is low, indicating that the PLA is a hard plastic. The PBTA tensile property is contrary to PLA; it possesses a high strain above 600% and a low modulus at approximately 15 Mpa, which is similar to thermal plastic elastomers. The stress-strain curves for PLA/PBAT blends show that the strain values at break increased with the PBAT content, but the stress values at break presented a reverse tendency, (Figure 6(a)). The PLA/PBAT (30/70), PLA/PBAT (50/50) and PLA/PBAT (70/30) exhibited a yield point; subsequently, they exhibited plastic elongation. These results indicate that the blends present greater softness than the PLA. Accordingly, the PBTA in the PLA/PBAT blends toughens the blends. The cross-section of SEM patterns shows relationships among the behavior of break, tensile properties, and morphologies of the samples. These samples underwent a quenched break under liquid nitrogen (Figures 7(a)–7(e)). The PLA under the quenched break showed a brittle and low-deformed break, and break tracks presented a considerable acute angle (Figure 7(a)). The PBAT also exhibited a brittle break, but its break angle was alleviative, and its break tracks were longer than PLA (Figure 7(b)). The break cross-sections of PLA/PBAT (70/30) and PLA/PBAT (50/50) were similar to that of PLA. The PLA/PBAT (70/30) presented an irregular-layer break cross-section and the PLA/PBAT (50/50) a directive-layer break cross-section (Figures 7(c) and 7(d)). The PLA/PBAT (30/70) showed that PLA was spheroid dispersed on a PBAT continuous phase, which is similar to the morphology of reinforcement for rubber toughness (Figure 7(e)). The PLA/PBAT (70/30) and PLA/PBAT (50/50) have lower elongation plastic deformation than the PLA/PBAT (30/70), as shown in the stress-strain curves in Figure 6(a). The PLA/PBAT (30/70) in all blends had the highest elongation (above 500%). The morphologies of blends on the effect of tensile strength are apparently revealed on the break cross-section of tensile testing at room temperature; the PLA and PBAT break cross-section, respectively, present an acute-angle section with fibrillose (Figure 8(a)) and slightly concave-convex plane morphologies (Figure 8(b)). The break cross-section for PLA/PBAT (70/30) and PLA/PBAT (50/50) presented numerous directive fiber shapes (Figures 8(c) and 8(d)). The bunch of directive fiber shapes under tensile testing at room temperature originates in the irregular and directive PLA-layer phase because the PLA layer phases undergo directional tensile force. The PLA layer phases are subsequently extracted from the PLA/PBAT mixed phase and broken (Figures 8(a)–8(e)). The break of acute angle and the bunch of fiber shape at the tensile break only appears in the PLA, PLA/PBAT (50/50), and PLA/PBAT (70/30) samples. However, the PLA/PBAT (30/70) exhibits an irregular concave break cross-section (Figure 8(e)), which has concave sizes within 100 um. The PLA/PBAT (30/70) presents an PLA irregular disperse phase that is dispersed in a PBAT continuous phase; that is, it has a sea-island morphology consisting of the PLA irregular island-phase and the PBTA sea-phase (Figure 8(e)). Because the PLA-dispersed phase is distributed over the PBAT continuous phase, which agrees with a toughened structure, the PLA/PBAT (30/70) has a higher elongation. Therefore, the PLA/PBAT (30/70) has a higher impact strength, as discussed in the following section.The tensile stress-strain curves of PLA/PBAT blends recorded at room temperature (27°C). (a) Untreated, (b) Annealed at 100°C for 8 hrs, (c) annealed at 100°C for 24 hrs.
(a)
(b)
(c)SEM graphs of break cross-section under the quenched break of liquid nitrogen. The white arrows in (a–d) point to the break tracks.
(a)
PLA
(b)
PBAT
(c)
PLA/PBAT (70/30)
(d)
PLA/PBAT (50/50)
(e)
PLA/PBAT (30/70)SEM graphs of break cross-section break on tensile testing at room temperature. The white arrows in (a–e) point to the break tracks.
(a)
PLA
(b)
PBAT
(c)
PLA/PBAT (50/50)
(d)
PLA/PBAT (70/30)
(e)
PLA/PBAT (30/70)


#### 3.2.2. Impact Strength

The components and morphologies of PLA/PBAT blends affect their impact strengths. Table4 shows the characteristics of impact at room temperature as determined by Izod Impact testing. The PLA, PLA/PBAT (70/30), and PLA/PBAT (50/50) exhibited an impact fracture, whereas PBAT and PLA/PBAT (30/70) had impact strength values (Kgf/cm) lower than those of  PLA/PBAT (30/70) and PBAT. The impact strength of PLA/PBAT blends increased with the PBAT content. The impact strength of PLA/PBAT (30/70) was slightly higher than that of PBAT. This result indicates that the morphologies of the PLA/PBAT blends have a significant effect on the impact strength, except for the PBAT content of the blend. As mentioned, the PLA/PBAT (30/70) exhibits an irregular sea-island morphology that has the effect of rubber toughening. Therefore, the PLA/PBAT (30/70) possesses a high impact strength. The impact strength of PLA/PBAT (50/50) is lower than that of PLA/PBAT (30/70), because PLA/PBAT (50/50) has a directive layer morphology (Figure 7(d)), and PLA/PBAT (70/30) has an irregular-layer morphology, even if PLA/PBAT (50/50) has a higher PBAT content than the PLA/PBAT (70/30). The morphologies of PLA/PBAT (50/50) and PLA/PBAT (70/30) after impact testing at room temperature are an acute angle break cross-section with a directive layer (Figures 9(a) and 9(b)), but the PLA/PBAT (50/50) has a higher directive layer than the PLA/PBAT (70/30). The PLA/PBAT (50/50) break cross-section also shows a concave region with long narrow edge. The patterns of appearing in the break cross-section confirm that the irregular and directive layer morphologies for PLA/PBAT (50/50) and PLA/PBAT (70/30) result from the PLA fiber shape (Figures 8 and 9). Although PLA has no obvious fiber shape or directive morphology, it presents the break further of acute angle and has a high degree of crystallization (Figure 9(c)). Therefore, the PLA has a lower impact strength compared to  PLA/PBAT (50/50) and PLA/PBAT (70/30) blends. The results in this section indicate that the PBAT content in blends and the morphologies of blends improve the impact strength of PLA.SEM micrographs of impact fractured at room temperature. The white arrows in (a-b) point to the break tracks.
(a)
PLA/PBAT (50/50)
(b)
PLA/PBAT (70/30)
(c)
PLA


### 3.3. Effect of Annealing on the Mechanical Properties

Annealing generally has a positive effect on improving mechanical properties. All samples in this study were undergone annealing at 100°C for 8 h and 24 h. Figures6(b)–6(c) and Table 4 show their tensile strength and impact strength. The initial modulus and the stress at break for PLA/PBAT blends increased after annealing, but their strain at break and impact strength decreased. These results are likely due to crystallization and the morphology. According to the DSC and WAXD results, annealing increased the degree of crystallization for PLA/PBAT blends and PLA. Accordingly, the morphology and degree of crystallization have negative effect on the impact strength of PLA/PBAT blends (Table 4). After annealing, the impact strength of PLA/PBAT blends decreased compared to those of the PLA and PBAT. This is likely because the PLA/PBAT (70/30) and PLA/PBAT (50/50) had fiber-shaped morphologies. Therefore, the development of crystallization for the PLA/PBAT (70/30) and PLA/PBAT (50/50) under the annealing process is along the direction of a bunch of fiber shapes. Accordingly, the directive crystallinity of blends increases their strength and initial modulus but reduces the elongation of the blend. However, the impact strength of PLA/PBAT (70/30) and PLA/PBAT (50/50) after annealing decreases because of the directive crystallinity resulting from the fiber-shape morphology (Table 4 and Figure 8). As the directive crystallinity in the blends undergoes impact force, a crack will result in array along the direction of crystallization. Accordingly, the blends present an acute-angle break cross-section with a directive layer morphology (Figures 9(a) and 9(b)). Similarly, the impact strength of PLA/PBAT (30/70) after annealing decreases because of a high degree of PLA crystallinity, island-phase morphology, and amorphous PBAT sea phase. The morphology of rubber toughening is generally caused by rubber particles dispersed in the continuous phase of the plastic. Rubber has a high elongation ability and impact strength, but its modulus is low. Therefore, it is easy to elongate along the stress direction, and the load is primarily borne by the continuous phase of the plastic [16]. The morphology of PLA/PBAT (30/70) is the opposite of rubber toughening; the PBAT continuous phase bears most of the load, and the PLA dispersed phase plays the role of reinforcement. Therefore, the untreated PLA/PBAT (30/70) has a high impact strength and good elongation ability but its high degree of crystallization after annealing causes a low impact strength and low tensile strength. However, the high degree of crystallization after annealing improves its heat deflection temperature (HDT) (Figure 10). Thus, the PLA HDT increases after annealing. The effect of crystallinity on the HDT is revealed on the degree of improvement for the blends and  HDT is very lower than the PLA. The PBAT decreases after annealing, and the PLA exhibits a high degree of crystallinity, according to the results of WAXD and DSC. Accordingly, the HDT is significantly affected by the degree of crystallization. However, the morphology of the blends has obvious effect. After annealing for 24 h, the PLA HDT reaches 128.5°C, which is a significant improvement over the PLA HDT.Figure 10
Relationship between heat deformation temperature and  composition of the PLA/PBAT.Figure 11
POM micrograph of PLA/PBAT (30/70) in the quenching process.


## 3.1. Phase Transition Regions and Miscibility

Semicrystalline polymers possess amorphous and crystalline phases, each of which has at least a phase transition region, that is, a glass transition temperature (Tg) and a melting temperature (Tm). The phase transition regions can be determined by DSC analysis, revealing the miscibility of polymer blends. A miscible polymer blend is homogeneous and usually displays a single Tg between those of the pure components, whereas a compatible blend shows both Tgs although these eventually shift toward one another.The thermograms of all samples in the initial and melt-quenched scans have several endothermic regions (Figures1 and 2). Table 1 lists the characteristic temperatures of glass transition regions for all samples. The glass transition temperatures (Tg) in this study were determined by the half-heat capacity (1/2  Cp) in the glass transition region. The PLA in the initial and melt-quenched DSC thermograms showed a Tg and Tm of 60°C and 165°C, respectively, whereas the PBAT displayed  Tg and Tm of approximately −33°C and 112°C, respectively (Tables 2 and 3). This result shows that PLA and PBAT are biodegradable crystalline plastics with amorphous and crystalline phases. The PBAT has a lower Tg broader Tm region than PLA (Figures 1 and 2) and provides good softness and impact resistance.Table 1
Characteristic temperatures of phase transition and enthalpy values of PLA/PBAT blends in the initial scan of DSC.
Code
T
g
-PBAT
1
T
g
-PLA
2
Δ
T
g
3
Δ
H
cc
4 (J/g)
T
m
-PLA
5 (°C)
Δ
H
m
-PLA
5 (J/g)
PLA
—
60.7
—
-
17.39
164.1
37
PLA/PBAT (70/30)
-
32.1
59.7
91.8
-
13.71
164.3
22.38
PLA/PBAT (50/50)
-
32.8
59.2
91.0
-
7.39
163.9
16.58
PLA/PBAT (30/70)
-
30.9
57.6
88.5
-
3.61
163.7
9.91
PBAT
−34
—
—
1
T
g
-PBAT: The temperature of glass transition region of PBAT.
2
T
g
-PLA: The temperature of glass transition region of PLA.
3
Δ
T
g: ΔTg=Tg-PLA-Tg-PBAT.
4
Δ
H
cc: The exothermal enthalpy of PLA cold-crystallization (re-crystallization).
5
T
m
-PLA  and ΔHm-PLA: The melting temperature and crystal melting enthalpy of PLA.Table 2
Characteristic temperatures of phase transition and enthalpy values of PLA/PBAT blends in the melt-quenched scan of DSC.
Code
T
g
-PBAT
1
T
g
-PLA
2
Δ
T
g
3
Δ
H
cc
4 (J/g)
T
m
-PLA
5 (°C)
Δ
H
m
-PLA
5 (J/g)
PLA
—
59.2
—
-
21.31
164.3
37.2
PLA/PBAT (70/30)
-
33.6
60.1
93.4
-
17.59
164.9
22.29
PLA/PBAT (50/50)
-
32.9
59.5
92.4
-
10.41
165.3
14.36
PLA/PBAT (30/70)
-
30.1
57.2
87.3
-
6.84
165.2
9.65
PBAT
−35.1
—
—
—
—
—
1
T
g
-PBAT: The temperature of glass transition region of PBAT.
2
T
g
-PLA: The temperature of glass transition region of PLA.
3
Δ
T
g: ΔTg=Tg-PLA-Tg-PBAT.
4
Δ
H
cc: The exothermal enthalpy of PLA cold-crystallization (re-crystallization).
5
T
m
-PLA and ΔHm-PLA: The melting temperature and crystal melting enthalpy of PLA.Table 3
The enthalpy and crystallinity of PLA/PBAT blends treated at 100°C for 8 and 24 hr.
Code
0 hr
8 hr
24 hr
Δ
H
m
a (J/g)
X
c
b  (%)
Δ
H
m
a (J/g)
X
c
b (%)
Δ
H
m
a (J/g)
X
c
b (%)
PLA
37
42.44
39.47
43.44
31.59
34
PLA/PBAT (70/30)
22.38
32.3
24.03
33.3
21.23
32.61
PLA/PBAT (50/50)
16.58
33.72
16.32
35.1
15.68
33.72
PLA/PBAT (30/70)
9.91
34.62
9.66
34.62
9.14
32.76
a
Δ
H
m: The crystal melting enthalpy of PLA.
b
X
c: The degree of crystallinity (Xc) of PLA.Figure 1
Initial scanning DSC thermogram of PLA/PBAT blends.Figure 2
Melt-quenched scanning DSC thermogram of PLA/PBAT blends.


### 3.1.1. Glass Transition Region of Blends

The PLA/PBAT blends in the initial and melt-quenched scan exhibit 2 glass transition regions at approximately −35 to −30°C and 57 to 61°C. These regions are, respectively, associated with PBAT and PLATg  (Tg-PBAT and Tg-PLA) regions (Figures 1 and 2). The PLA/PBAT blends exhibit two Tg  regions, indicating that the blends are immiscible and present a two-phase structure. However, the Tg-PBAT and Tg-PLA values for various PLA/PBAT blends in the initial and melt-quenched scans changed in a small region at approximately −30 to −35°C and 57 to 61°C, respectively (Tables 1 and 2). Accordingly, the PLA and PBAT in the PLA/PBAT blends present a low compatibility. The ΔTg (Tg-PLA–Tg-PBAT) represents the degree of compatibility, which is affected by its morphology. The PLA/PBAT (30/70) has the lowest ΔTg value, and the ΔTg values for both PLA/PBAT (70/30) and PLA/PBAT (50/50) are relatively similar (Tables 1 and 2). This result indicates that the blends have at least two morphologies. The following SEM analysis presents the phase-separation structure and morphologies of these samples.The PLA/PBAT blends that underwent the melt-quenched process determine the compatibility of the blends and their phase-separation behavior. TheTg values (Tg-PBAT and Tg-PLA) under the melt-quenched scan for PLA and PBAT appeared to decrease slightly, and their Tg regions were broader than the initial scan (Table 1 and Figures 1 and 2). This result indicates that the amorphousness of PBAT and PLA increased under the melt-quenched process. The Tg regions in PLA/PBAT blends after the melt-quenched scan also show two Tg regions associated with the PBAT and PLA Tg regions, respectively. The ΔTg, Tg-PBAT, and Tg-PLA values for PLA/PBAT blends after the melt-quenched process have exhibited a slight variation within the region of 2°C (Tables 1 and 2). Therefore, the morphologies of the blends are two-phase structures, and the compatibility of blends is low because the Tg values have no obvious variation after the melt quenching process. Spinodal decomposition (SD) is a mechanism for the rapid unmixing of a mixture of liquids or solids from one thermodynamic phase to form two coexisting phases during rapid cooling process [14]. The two-phase separation of PLA/PBAT blends is due to SD during proceeding in the quenching process [15]. The morphology of PLA/PBAT (30/70) structure after the quenching process was presented by a polarized optical microscope (POM) (Figure 11). It can be seen that PLA/PBAT blends exhibited the irregularly interwoven phase. As reported previously, SD typically yields an interwoven structure [16]. Thus, it might be implied that the morphology of PLA/PBAT was attributed to SD in the quenching process. The thermograms of Tg region for PLA at approximately 63°C show a melt-like peak, which disappears under melt-quenched scanning (Figures 1 and 2). This result suggests an enthalpy relaxation resulting from physical aging of PLA amorphous macromolecular chains [17]. This aging process involves certain local density changes of the amorphous phase, generating nuclei and facilitating the crystallization of PLA [18].


### 3.1.2. Melting Transition Region

The crystal-melting temperature of PLA (Tm-PLA) in the initial scan presented melting at approximately 164°C, but the PBAT had no obvious melting endothermic region (Figure 1). The PLA/PBAT blends in the initial scanning displayed a crystal-melting endothermic region at approximately 164°C, and the enthalpy values in the initial scanning for the PLA/PBAT blends increased almost linearly as the PLA content increased (Table 2). Accordingly, the melting endothermic region of PLA/PBAT blends is associated with PLA crystallization. The melting-temperature (Tm-PLA) regions of the PLA and PLA/PBAT blends after melt-quenched scanning remained at approximately 164°C, and their crystal-melting enthalpy (ΔHm) values showed no obvious change (Tables 1 and 2). The uniform ΔHm values before and after melted-quenched scanning (Tables 1 and 2) indicate that the PLA in the PLA/PBAT blends has a high rate of crystallization or high crystallization ability. These results illustrate a high degree of phase separation for the PLA/PBAT because the crystallization ability does not change significantly under the melt quenching process. Therefore, the PLA and PBAT in the blends tend to form independent phases. The PLA and PLA/PBAT blends in the DSC curves at approximately 80–100°C under the initial and melt-quenched scans exhibit that an exothermal peak is associated with PLA recrystallization (cold crystallization). This is because the PLA in all samples has the only crystallization ability. This PLA recrystallization likely results from the cold crystallization processes of PLA because the cold crystallization only presents a polymer with a high crystallization ability. The region of the cold crystallization temperature and the enthalpies (ΔHcc) of crystal exothermal peak were almost uniform under the initial and melt-quenched scanning (Tables 1 and 2), indicating that the PBAT composition in the blends hardly affects the crystallization ability of PLA. Thus, the PLA and PBAT in the PLA/PBAT blends tend to form independent phase. Accordingly, the PLA/PBAT blends should exhibit a two-phase structure, as further verified in SEM analysis.To further investigate the crystalline characteristics of PLA/PBAT blends, all samples were annealed at 100°C for 8 and 24 h and were analyzed using DSC and WAXD. Figure3 shows that the melting temperatures of PLA/PBAT blends remained at approximately 164°C, indicating that their crystalline form remained unchanged by the annealing process. However, the enthalpy of melting crystal (ΔHm) and degree of crystallization (Xc) for the PLA/PBAT blends increased after annealing (Table 4). The ΔHm and Xc reached their maximum values after annealing at 100°C for 8 h and underwent thermal aging when annealed for longer times (24 h) as observed from the drop in crystallinity values. This increase in the ΔHm and Xc values might result from the high-oriented amorphous PLA macromolecular chains, which can easily incorporate the PLA crystalline lattice. Therefore, the PLA macromolecular chains with a high orientation recrystallize (cool-crystallize) at 80–100°C (Figures 1 and 3). The cool-crystalline structure disappeared after the annealing process (Figure 3), but Hm and Xc increased (Tables 1 and 2). These results verify that the macromolecular chains of high orientation merged with the raw crystals during the annealing process.Table 4
The impact strength (KJ/m) for all samples under the melt-quenching and various annealing.
Melt-quenching
Annealing at 100°C for 24 h
Annealing at 100°C for 8 h
Break after Izod impact Testing1
PLA
3.85
3.85
3.62
○
PLA/PBAT (70/30)
19.03
13.65
12.11
○
PLA/PBAT (50/50)
18.77
7.57
7.01
○
PLA/PBAT (30/70)
33.56
21.6
22.58
×
PBAT
30.5
30.75
29.24
×
○: Fracture.
×: Has not destroy.
1The extent of damage of sample after Izod impact testing.Figure 3
PLA/PBAT blends DSC annealing at 100°C for 8 hr.We also investigated the characteristics of the crystals and effects of annealing on the PBAT/PLA blends using WAXD (Figures4 and 5). Figure 4 shows that the WAXD curves for the untreated PLA present a strong diffraction peaks at 2θ=18.7° corresponding to the (203) crystal plane  [10]. The WAXD peaks for the untreated PLA/PBAT blends were almost the same as those for PLA, but the diffractive intensities of blends are lower than those of the PLA because of a low PLA content. Several small diffraction peaks appeared in all samples and might be associated with PLA microcrystallinity (Figure 4). The WAXD peaks of PLA and PLA/PBAT blends annealed for 8 h at 100°C exhibited strong diffraction peaks at 2θ=17.5°, except for 2θ=18.7°  (Figure 5). The maximum value of diffractive intensity for the PLA/PBAT blends in all diffraction peaks appears at 2θ = 17.5°  corresponding to the (200/110) crystal plane [10]. This result indicates that the PLA composition in the PLA/PBAT blends under the annealing process exhibits an orientation crystalline structure that originates in the amorphous PLA macromolecular chains of high orientation. The orientation of macromolecular chains in the study is caused by the shearing force under the mixed and injection-molding process. Accordingly, the ΔHm and Xc values of the PLA/PBAT blends annealed for 8 h and 24 h are higher than those  for untreated samples (Table 3). The ΔHm and Xc values of the PLA and PLA/PBAT blends annealed at 100°C for 24 h are slightly lower than those of samples annealed for 8 h (Table 3), verifying that the PLA crystal undergoes thermal aging when annealed at 100°C for 24 h. The amorphous PLA macromolecular chains of high orientation verify the effects of cool crystallization on the initial and melt-quenched DSC scanning. We use the PLA that is an extrusion grade plastic with a low crystallinity. Thus, although the DSC heating thermograms of the PLA did not show melting endothermal peak, its DSC cooling thermograms displayed a broad weak melting exothermal peak in the temperature range of 105–45°C (Figure 1(b)).Figure 4
WAXD patterns of the untreated P LA/PBAT blends.Figure 5
WAXD patterns of PLA/PBAT blends annealing at 100°C for 8 hrs.


## 3.1.1. Glass Transition Region of Blends

The PLA/PBAT blends in the initial and melt-quenched scan exhibit 2 glass transition regions at approximately −35 to −30°C and 57 to 61°C. These regions are, respectively, associated with PBAT and PLATg  (Tg-PBAT and Tg-PLA) regions (Figures 1 and 2). The PLA/PBAT blends exhibit two Tg  regions, indicating that the blends are immiscible and present a two-phase structure. However, the Tg-PBAT and Tg-PLA values for various PLA/PBAT blends in the initial and melt-quenched scans changed in a small region at approximately −30 to −35°C and 57 to 61°C, respectively (Tables 1 and 2). Accordingly, the PLA and PBAT in the PLA/PBAT blends present a low compatibility. The ΔTg (Tg-PLA–Tg-PBAT) represents the degree of compatibility, which is affected by its morphology. The PLA/PBAT (30/70) has the lowest ΔTg value, and the ΔTg values for both PLA/PBAT (70/30) and PLA/PBAT (50/50) are relatively similar (Tables 1 and 2). This result indicates that the blends have at least two morphologies. The following SEM analysis presents the phase-separation structure and morphologies of these samples.The PLA/PBAT blends that underwent the melt-quenched process determine the compatibility of the blends and their phase-separation behavior. TheTg values (Tg-PBAT and Tg-PLA) under the melt-quenched scan for PLA and PBAT appeared to decrease slightly, and their Tg regions were broader than the initial scan (Table 1 and Figures 1 and 2). This result indicates that the amorphousness of PBAT and PLA increased under the melt-quenched process. The Tg regions in PLA/PBAT blends after the melt-quenched scan also show two Tg regions associated with the PBAT and PLA Tg regions, respectively. The ΔTg, Tg-PBAT, and Tg-PLA values for PLA/PBAT blends after the melt-quenched process have exhibited a slight variation within the region of 2°C (Tables 1 and 2). Therefore, the morphologies of the blends are two-phase structures, and the compatibility of blends is low because the Tg values have no obvious variation after the melt quenching process. Spinodal decomposition (SD) is a mechanism for the rapid unmixing of a mixture of liquids or solids from one thermodynamic phase to form two coexisting phases during rapid cooling process [14]. The two-phase separation of PLA/PBAT blends is due to SD during proceeding in the quenching process [15]. The morphology of PLA/PBAT (30/70) structure after the quenching process was presented by a polarized optical microscope (POM) (Figure 11). It can be seen that PLA/PBAT blends exhibited the irregularly interwoven phase. As reported previously, SD typically yields an interwoven structure [16]. Thus, it might be implied that the morphology of PLA/PBAT was attributed to SD in the quenching process. The thermograms of Tg region for PLA at approximately 63°C show a melt-like peak, which disappears under melt-quenched scanning (Figures 1 and 2). This result suggests an enthalpy relaxation resulting from physical aging of PLA amorphous macromolecular chains [17]. This aging process involves certain local density changes of the amorphous phase, generating nuclei and facilitating the crystallization of PLA [18].


## 3.1.2. Melting Transition Region

The crystal-melting temperature of PLA (Tm-PLA) in the initial scan presented melting at approximately 164°C, but the PBAT had no obvious melting endothermic region (Figure 1). The PLA/PBAT blends in the initial scanning displayed a crystal-melting endothermic region at approximately 164°C, and the enthalpy values in the initial scanning for the PLA/PBAT blends increased almost linearly as the PLA content increased (Table 2). Accordingly, the melting endothermic region of PLA/PBAT blends is associated with PLA crystallization. The melting-temperature (Tm-PLA) regions of the PLA and PLA/PBAT blends after melt-quenched scanning remained at approximately 164°C, and their crystal-melting enthalpy (ΔHm) values showed no obvious change (Tables 1 and 2). The uniform ΔHm values before and after melted-quenched scanning (Tables 1 and 2) indicate that the PLA in the PLA/PBAT blends has a high rate of crystallization or high crystallization ability. These results illustrate a high degree of phase separation for the PLA/PBAT because the crystallization ability does not change significantly under the melt quenching process. Therefore, the PLA and PBAT in the blends tend to form independent phases. The PLA and PLA/PBAT blends in the DSC curves at approximately 80–100°C under the initial and melt-quenched scans exhibit that an exothermal peak is associated with PLA recrystallization (cold crystallization). This is because the PLA in all samples has the only crystallization ability. This PLA recrystallization likely results from the cold crystallization processes of PLA because the cold crystallization only presents a polymer with a high crystallization ability. The region of the cold crystallization temperature and the enthalpies (ΔHcc) of crystal exothermal peak were almost uniform under the initial and melt-quenched scanning (Tables 1 and 2), indicating that the PBAT composition in the blends hardly affects the crystallization ability of PLA. Thus, the PLA and PBAT in the PLA/PBAT blends tend to form independent phase. Accordingly, the PLA/PBAT blends should exhibit a two-phase structure, as further verified in SEM analysis.To further investigate the crystalline characteristics of PLA/PBAT blends, all samples were annealed at 100°C for 8 and 24 h and were analyzed using DSC and WAXD. Figure3 shows that the melting temperatures of PLA/PBAT blends remained at approximately 164°C, indicating that their crystalline form remained unchanged by the annealing process. However, the enthalpy of melting crystal (ΔHm) and degree of crystallization (Xc) for the PLA/PBAT blends increased after annealing (Table 4). The ΔHm and Xc reached their maximum values after annealing at 100°C for 8 h and underwent thermal aging when annealed for longer times (24 h) as observed from the drop in crystallinity values. This increase in the ΔHm and Xc values might result from the high-oriented amorphous PLA macromolecular chains, which can easily incorporate the PLA crystalline lattice. Therefore, the PLA macromolecular chains with a high orientation recrystallize (cool-crystallize) at 80–100°C (Figures 1 and 3). The cool-crystalline structure disappeared after the annealing process (Figure 3), but Hm and Xc increased (Tables 1 and 2). These results verify that the macromolecular chains of high orientation merged with the raw crystals during the annealing process.Table 4
The impact strength (KJ/m) for all samples under the melt-quenching and various annealing.
Melt-quenching
Annealing at 100°C for 24 h
Annealing at 100°C for 8 h
Break after Izod impact Testing1
PLA
3.85
3.85
3.62
○
PLA/PBAT (70/30)
19.03
13.65
12.11
○
PLA/PBAT (50/50)
18.77
7.57
7.01
○
PLA/PBAT (30/70)
33.56
21.6
22.58
×
PBAT
30.5
30.75
29.24
×
○: Fracture.
×: Has not destroy.
1The extent of damage of sample after Izod impact testing.Figure 3
PLA/PBAT blends DSC annealing at 100°C for 8 hr.We also investigated the characteristics of the crystals and effects of annealing on the PBAT/PLA blends using WAXD (Figures4 and 5). Figure 4 shows that the WAXD curves for the untreated PLA present a strong diffraction peaks at 2θ=18.7° corresponding to the (203) crystal plane  [10]. The WAXD peaks for the untreated PLA/PBAT blends were almost the same as those for PLA, but the diffractive intensities of blends are lower than those of the PLA because of a low PLA content. Several small diffraction peaks appeared in all samples and might be associated with PLA microcrystallinity (Figure 4). The WAXD peaks of PLA and PLA/PBAT blends annealed for 8 h at 100°C exhibited strong diffraction peaks at 2θ=17.5°, except for 2θ=18.7°  (Figure 5). The maximum value of diffractive intensity for the PLA/PBAT blends in all diffraction peaks appears at 2θ = 17.5°  corresponding to the (200/110) crystal plane [10]. This result indicates that the PLA composition in the PLA/PBAT blends under the annealing process exhibits an orientation crystalline structure that originates in the amorphous PLA macromolecular chains of high orientation. The orientation of macromolecular chains in the study is caused by the shearing force under the mixed and injection-molding process. Accordingly, the ΔHm and Xc values of the PLA/PBAT blends annealed for 8 h and 24 h are higher than those  for untreated samples (Table 3). The ΔHm and Xc values of the PLA and PLA/PBAT blends annealed at 100°C for 24 h are slightly lower than those of samples annealed for 8 h (Table 3), verifying that the PLA crystal undergoes thermal aging when annealed at 100°C for 24 h. The amorphous PLA macromolecular chains of high orientation verify the effects of cool crystallization on the initial and melt-quenched DSC scanning. We use the PLA that is an extrusion grade plastic with a low crystallinity. Thus, although the DSC heating thermograms of the PLA did not show melting endothermal peak, its DSC cooling thermograms displayed a broad weak melting exothermal peak in the temperature range of 105–45°C (Figure 1(b)).Figure 4
WAXD patterns of the untreated P LA/PBAT blends.Figure 5
WAXD patterns of PLA/PBAT blends annealing at 100°C for 8 hrs.


## 3.2. Mechanical Properties and Morphologies

As mentioned in the DSC and WAXD analyses, the PLA in the blends was a semicrystalline polymer with a high crystallization ability. Conversely, the PBAT presented features of an amorphous polymer. The PLA/PBAT blends had two-phase structure. The compatibility and morphology of the blends, which are associated with their components, determine the mechanical properties such as tensile and impact strength. This section presents the relationships between mechanical properties and morphologies as revealed by tensile strength and impact strength tests.


### 3.2.1. Tensile Strength

Figure6(a) shows the stress-strain curves of all untreated samples at room temperature. PLA has a high stress and high initial modulus, but its strain is low, indicating that the PLA is a hard plastic. The PBTA tensile property is contrary to PLA; it possesses a high strain above 600% and a low modulus at approximately 15 Mpa, which is similar to thermal plastic elastomers. The stress-strain curves for PLA/PBAT blends show that the strain values at break increased with the PBAT content, but the stress values at break presented a reverse tendency, (Figure 6(a)). The PLA/PBAT (30/70), PLA/PBAT (50/50) and PLA/PBAT (70/30) exhibited a yield point; subsequently, they exhibited plastic elongation. These results indicate that the blends present greater softness than the PLA. Accordingly, the PBTA in the PLA/PBAT blends toughens the blends. The cross-section of SEM patterns shows relationships among the behavior of break, tensile properties, and morphologies of the samples. These samples underwent a quenched break under liquid nitrogen (Figures 7(a)–7(e)). The PLA under the quenched break showed a brittle and low-deformed break, and break tracks presented a considerable acute angle (Figure 7(a)). The PBAT also exhibited a brittle break, but its break angle was alleviative, and its break tracks were longer than PLA (Figure 7(b)). The break cross-sections of PLA/PBAT (70/30) and PLA/PBAT (50/50) were similar to that of PLA. The PLA/PBAT (70/30) presented an irregular-layer break cross-section and the PLA/PBAT (50/50) a directive-layer break cross-section (Figures 7(c) and 7(d)). The PLA/PBAT (30/70) showed that PLA was spheroid dispersed on a PBAT continuous phase, which is similar to the morphology of reinforcement for rubber toughness (Figure 7(e)). The PLA/PBAT (70/30) and PLA/PBAT (50/50) have lower elongation plastic deformation than the PLA/PBAT (30/70), as shown in the stress-strain curves in Figure 6(a). The PLA/PBAT (30/70) in all blends had the highest elongation (above 500%). The morphologies of blends on the effect of tensile strength are apparently revealed on the break cross-section of tensile testing at room temperature; the PLA and PBAT break cross-section, respectively, present an acute-angle section with fibrillose (Figure 8(a)) and slightly concave-convex plane morphologies (Figure 8(b)). The break cross-section for PLA/PBAT (70/30) and PLA/PBAT (50/50) presented numerous directive fiber shapes (Figures 8(c) and 8(d)). The bunch of directive fiber shapes under tensile testing at room temperature originates in the irregular and directive PLA-layer phase because the PLA layer phases undergo directional tensile force. The PLA layer phases are subsequently extracted from the PLA/PBAT mixed phase and broken (Figures 8(a)–8(e)). The break of acute angle and the bunch of fiber shape at the tensile break only appears in the PLA, PLA/PBAT (50/50), and PLA/PBAT (70/30) samples. However, the PLA/PBAT (30/70) exhibits an irregular concave break cross-section (Figure 8(e)), which has concave sizes within 100 um. The PLA/PBAT (30/70) presents an PLA irregular disperse phase that is dispersed in a PBAT continuous phase; that is, it has a sea-island morphology consisting of the PLA irregular island-phase and the PBTA sea-phase (Figure 8(e)). Because the PLA-dispersed phase is distributed over the PBAT continuous phase, which agrees with a toughened structure, the PLA/PBAT (30/70) has a higher elongation. Therefore, the PLA/PBAT (30/70) has a higher impact strength, as discussed in the following section.The tensile stress-strain curves of PLA/PBAT blends recorded at room temperature (27°C). (a) Untreated, (b) Annealed at 100°C for 8 hrs, (c) annealed at 100°C for 24 hrs.
(a)
(b)
(c)SEM graphs of break cross-section under the quenched break of liquid nitrogen. The white arrows in (a–d) point to the break tracks.
(a)
PLA
(b)
PBAT
(c)
PLA/PBAT (70/30)
(d)
PLA/PBAT (50/50)
(e)
PLA/PBAT (30/70)SEM graphs of break cross-section break on tensile testing at room temperature. The white arrows in (a–e) point to the break tracks.
(a)
PLA
(b)
PBAT
(c)
PLA/PBAT (50/50)
(d)
PLA/PBAT (70/30)
(e)
PLA/PBAT (30/70)


### 3.2.2. Impact Strength

The components and morphologies of PLA/PBAT blends affect their impact strengths. Table4 shows the characteristics of impact at room temperature as determined by Izod Impact testing. The PLA, PLA/PBAT (70/30), and PLA/PBAT (50/50) exhibited an impact fracture, whereas PBAT and PLA/PBAT (30/70) had impact strength values (Kgf/cm) lower than those of  PLA/PBAT (30/70) and PBAT. The impact strength of PLA/PBAT blends increased with the PBAT content. The impact strength of PLA/PBAT (30/70) was slightly higher than that of PBAT. This result indicates that the morphologies of the PLA/PBAT blends have a significant effect on the impact strength, except for the PBAT content of the blend. As mentioned, the PLA/PBAT (30/70) exhibits an irregular sea-island morphology that has the effect of rubber toughening. Therefore, the PLA/PBAT (30/70) possesses a high impact strength. The impact strength of PLA/PBAT (50/50) is lower than that of PLA/PBAT (30/70), because PLA/PBAT (50/50) has a directive layer morphology (Figure 7(d)), and PLA/PBAT (70/30) has an irregular-layer morphology, even if PLA/PBAT (50/50) has a higher PBAT content than the PLA/PBAT (70/30). The morphologies of PLA/PBAT (50/50) and PLA/PBAT (70/30) after impact testing at room temperature are an acute angle break cross-section with a directive layer (Figures 9(a) and 9(b)), but the PLA/PBAT (50/50) has a higher directive layer than the PLA/PBAT (70/30). The PLA/PBAT (50/50) break cross-section also shows a concave region with long narrow edge. The patterns of appearing in the break cross-section confirm that the irregular and directive layer morphologies for PLA/PBAT (50/50) and PLA/PBAT (70/30) result from the PLA fiber shape (Figures 8 and 9). Although PLA has no obvious fiber shape or directive morphology, it presents the break further of acute angle and has a high degree of crystallization (Figure 9(c)). Therefore, the PLA has a lower impact strength compared to  PLA/PBAT (50/50) and PLA/PBAT (70/30) blends. The results in this section indicate that the PBAT content in blends and the morphologies of blends improve the impact strength of PLA.SEM micrographs of impact fractured at room temperature. The white arrows in (a-b) point to the break tracks.
(a)
PLA/PBAT (50/50)
(b)
PLA/PBAT (70/30)
(c)
PLA


## 3.2.1. Tensile Strength

Figure6(a) shows the stress-strain curves of all untreated samples at room temperature. PLA has a high stress and high initial modulus, but its strain is low, indicating that the PLA is a hard plastic. The PBTA tensile property is contrary to PLA; it possesses a high strain above 600% and a low modulus at approximately 15 Mpa, which is similar to thermal plastic elastomers. The stress-strain curves for PLA/PBAT blends show that the strain values at break increased with the PBAT content, but the stress values at break presented a reverse tendency, (Figure 6(a)). The PLA/PBAT (30/70), PLA/PBAT (50/50) and PLA/PBAT (70/30) exhibited a yield point; subsequently, they exhibited plastic elongation. These results indicate that the blends present greater softness than the PLA. Accordingly, the PBTA in the PLA/PBAT blends toughens the blends. The cross-section of SEM patterns shows relationships among the behavior of break, tensile properties, and morphologies of the samples. These samples underwent a quenched break under liquid nitrogen (Figures 7(a)–7(e)). The PLA under the quenched break showed a brittle and low-deformed break, and break tracks presented a considerable acute angle (Figure 7(a)). The PBAT also exhibited a brittle break, but its break angle was alleviative, and its break tracks were longer than PLA (Figure 7(b)). The break cross-sections of PLA/PBAT (70/30) and PLA/PBAT (50/50) were similar to that of PLA. The PLA/PBAT (70/30) presented an irregular-layer break cross-section and the PLA/PBAT (50/50) a directive-layer break cross-section (Figures 7(c) and 7(d)). The PLA/PBAT (30/70) showed that PLA was spheroid dispersed on a PBAT continuous phase, which is similar to the morphology of reinforcement for rubber toughness (Figure 7(e)). The PLA/PBAT (70/30) and PLA/PBAT (50/50) have lower elongation plastic deformation than the PLA/PBAT (30/70), as shown in the stress-strain curves in Figure 6(a). The PLA/PBAT (30/70) in all blends had the highest elongation (above 500%). The morphologies of blends on the effect of tensile strength are apparently revealed on the break cross-section of tensile testing at room temperature; the PLA and PBAT break cross-section, respectively, present an acute-angle section with fibrillose (Figure 8(a)) and slightly concave-convex plane morphologies (Figure 8(b)). The break cross-section for PLA/PBAT (70/30) and PLA/PBAT (50/50) presented numerous directive fiber shapes (Figures 8(c) and 8(d)). The bunch of directive fiber shapes under tensile testing at room temperature originates in the irregular and directive PLA-layer phase because the PLA layer phases undergo directional tensile force. The PLA layer phases are subsequently extracted from the PLA/PBAT mixed phase and broken (Figures 8(a)–8(e)). The break of acute angle and the bunch of fiber shape at the tensile break only appears in the PLA, PLA/PBAT (50/50), and PLA/PBAT (70/30) samples. However, the PLA/PBAT (30/70) exhibits an irregular concave break cross-section (Figure 8(e)), which has concave sizes within 100 um. The PLA/PBAT (30/70) presents an PLA irregular disperse phase that is dispersed in a PBAT continuous phase; that is, it has a sea-island morphology consisting of the PLA irregular island-phase and the PBTA sea-phase (Figure 8(e)). Because the PLA-dispersed phase is distributed over the PBAT continuous phase, which agrees with a toughened structure, the PLA/PBAT (30/70) has a higher elongation. Therefore, the PLA/PBAT (30/70) has a higher impact strength, as discussed in the following section.The tensile stress-strain curves of PLA/PBAT blends recorded at room temperature (27°C). (a) Untreated, (b) Annealed at 100°C for 8 hrs, (c) annealed at 100°C for 24 hrs.
(a)
(b)
(c)SEM graphs of break cross-section under the quenched break of liquid nitrogen. The white arrows in (a–d) point to the break tracks.
(a)
PLA
(b)
PBAT
(c)
PLA/PBAT (70/30)
(d)
PLA/PBAT (50/50)
(e)
PLA/PBAT (30/70)SEM graphs of break cross-section break on tensile testing at room temperature. The white arrows in (a–e) point to the break tracks.
(a)
PLA
(b)
PBAT
(c)
PLA/PBAT (50/50)
(d)
PLA/PBAT (70/30)
(e)
PLA/PBAT (30/70)


## 3.2.2. Impact Strength

The components and morphologies of PLA/PBAT blends affect their impact strengths. Table4 shows the characteristics of impact at room temperature as determined by Izod Impact testing. The PLA, PLA/PBAT (70/30), and PLA/PBAT (50/50) exhibited an impact fracture, whereas PBAT and PLA/PBAT (30/70) had impact strength values (Kgf/cm) lower than those of  PLA/PBAT (30/70) and PBAT. The impact strength of PLA/PBAT blends increased with the PBAT content. The impact strength of PLA/PBAT (30/70) was slightly higher than that of PBAT. This result indicates that the morphologies of the PLA/PBAT blends have a significant effect on the impact strength, except for the PBAT content of the blend. As mentioned, the PLA/PBAT (30/70) exhibits an irregular sea-island morphology that has the effect of rubber toughening. Therefore, the PLA/PBAT (30/70) possesses a high impact strength. The impact strength of PLA/PBAT (50/50) is lower than that of PLA/PBAT (30/70), because PLA/PBAT (50/50) has a directive layer morphology (Figure 7(d)), and PLA/PBAT (70/30) has an irregular-layer morphology, even if PLA/PBAT (50/50) has a higher PBAT content than the PLA/PBAT (70/30). The morphologies of PLA/PBAT (50/50) and PLA/PBAT (70/30) after impact testing at room temperature are an acute angle break cross-section with a directive layer (Figures 9(a) and 9(b)), but the PLA/PBAT (50/50) has a higher directive layer than the PLA/PBAT (70/30). The PLA/PBAT (50/50) break cross-section also shows a concave region with long narrow edge. The patterns of appearing in the break cross-section confirm that the irregular and directive layer morphologies for PLA/PBAT (50/50) and PLA/PBAT (70/30) result from the PLA fiber shape (Figures 8 and 9). Although PLA has no obvious fiber shape or directive morphology, it presents the break further of acute angle and has a high degree of crystallization (Figure 9(c)). Therefore, the PLA has a lower impact strength compared to  PLA/PBAT (50/50) and PLA/PBAT (70/30) blends. The results in this section indicate that the PBAT content in blends and the morphologies of blends improve the impact strength of PLA.SEM micrographs of impact fractured at room temperature. The white arrows in (a-b) point to the break tracks.
(a)
PLA/PBAT (50/50)
(b)
PLA/PBAT (70/30)
(c)
PLA


## 3.3. Effect of Annealing on the Mechanical Properties

Annealing generally has a positive effect on improving mechanical properties. All samples in this study were undergone annealing at 100°C for 8 h and 24 h. Figures6(b)–6(c) and Table 4 show their tensile strength and impact strength. The initial modulus and the stress at break for PLA/PBAT blends increased after annealing, but their strain at break and impact strength decreased. These results are likely due to crystallization and the morphology. According to the DSC and WAXD results, annealing increased the degree of crystallization for PLA/PBAT blends and PLA. Accordingly, the morphology and degree of crystallization have negative effect on the impact strength of PLA/PBAT blends (Table 4). After annealing, the impact strength of PLA/PBAT blends decreased compared to those of the PLA and PBAT. This is likely because the PLA/PBAT (70/30) and PLA/PBAT (50/50) had fiber-shaped morphologies. Therefore, the development of crystallization for the PLA/PBAT (70/30) and PLA/PBAT (50/50) under the annealing process is along the direction of a bunch of fiber shapes. Accordingly, the directive crystallinity of blends increases their strength and initial modulus but reduces the elongation of the blend. However, the impact strength of PLA/PBAT (70/30) and PLA/PBAT (50/50) after annealing decreases because of the directive crystallinity resulting from the fiber-shape morphology (Table 4 and Figure 8). As the directive crystallinity in the blends undergoes impact force, a crack will result in array along the direction of crystallization. Accordingly, the blends present an acute-angle break cross-section with a directive layer morphology (Figures 9(a) and 9(b)). Similarly, the impact strength of PLA/PBAT (30/70) after annealing decreases because of a high degree of PLA crystallinity, island-phase morphology, and amorphous PBAT sea phase. The morphology of rubber toughening is generally caused by rubber particles dispersed in the continuous phase of the plastic. Rubber has a high elongation ability and impact strength, but its modulus is low. Therefore, it is easy to elongate along the stress direction, and the load is primarily borne by the continuous phase of the plastic [16]. The morphology of PLA/PBAT (30/70) is the opposite of rubber toughening; the PBAT continuous phase bears most of the load, and the PLA dispersed phase plays the role of reinforcement. Therefore, the untreated PLA/PBAT (30/70) has a high impact strength and good elongation ability but its high degree of crystallization after annealing causes a low impact strength and low tensile strength. However, the high degree of crystallization after annealing improves its heat deflection temperature (HDT) (Figure 10). Thus, the PLA HDT increases after annealing. The effect of crystallinity on the HDT is revealed on the degree of improvement for the blends and  HDT is very lower than the PLA. The PBAT decreases after annealing, and the PLA exhibits a high degree of crystallinity, according to the results of WAXD and DSC. Accordingly, the HDT is significantly affected by the degree of crystallization. However, the morphology of the blends has obvious effect. After annealing for 24 h, the PLA HDT reaches 128.5°C, which is a significant improvement over the PLA HDT.Figure 10
Relationship between heat deformation temperature and  composition of the PLA/PBAT.Figure 11
POM micrograph of PLA/PBAT (30/70) in the quenching process.


## 4. Conclusion

The PLA/PBAT blends in the DSC analysis exhibit two glass transition regions, indicating that the blends are immiscible. Therefore, the PLA/PBAT blends have a two-phase structure. The morphologies of the two-phase structure for PLA/PBAT (30/70), PLA/PBAT (50/50), and PLA/PBAT (70/30) blends in the SEM, respectively, exhibit sea-island, directive layer, and irregular-layer morphologies, respectively. The morphology of PLA/PBAT (50/50) showed a major effect on the mechanical properties. The PLA/PBAT (70/30) composition has higher impact strength than PLA/PBAT (50/50) composition. This result is because the PLA/PBAT (50/50) has directive layer morphology. Accordingly, the morphology of PLA/PBA blends has a significant effect on mechanical properties, except for the PBAT content. The mechanical properties of PLA exhibit low-strain and high-stress characteristics; therefore, the toughness of PLA is low in practical applications. Conversely, PBAT presents a low stress but has high strain. Accordingly, low-strain and high-stress properties of the PLA are complementary with elastomeric of the PBAT. Both morphology and composition of the blends are determinants of their impact strength. In this study, the PLA/PBAT (30/70) blends are an optimal condition that it presents the highest elongation, better impact strength with sea-island morphology. Annealing increased the degree of crystallization in the blends, raising their initial modulus, stress, and HDT, but reducing their impact strength. The directive layer morphology of the blends produced a directive crystal causing the large decrease in impact strength after annealing.



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*Source: 951696-2013-09-09.xml*