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User Benefits Application News Fig. 1 AGX -V2 Virgin homopolypropylene was used as the material. Pellets prepared by applying the advanced recycling process to virgin homopolypropylene after simulated degradation by shearing multiple times in a kneading machine, and pellets of the same material without the advanced recycling process were used as the samples. These two types of pellets were molded to the ISO 527-2 1A and ASTM D1822 Type L test piece shapes by injection molding. Table 1 shows the test piece shapes and the types of evaluations conducted. Test Pieces Table 1 Test Piece Shapes and Evaluations Conducted Table 2 Instrument Configuration and Test Conditions In the previously-published Application News article “Multifaceted Evaluation of Changes in Physical Properties of Recycled Plastics by Advanced Recycling Process and Influencing Microstructural Changes (Part 1),” it was found that the microscopic physical structure of recycled polyethylene (PE) was controlled by applying a new advanced recycling process, and as a result, the strain at break and the impact property improved. That study also demonstrated that a multifaceted evaluation combining the elastic modulus, indentation hardness (H IT ), crystallization start temperature, and orientation and structural information in the micro region is an effective approach for understanding the changes in the microscopic physical structure. Here, the same multifaceted evaluation was carried out for simulated degraded polypropylene (PP), and the changes in the physical properties and the microscopic physical structure were analyzed. Introduction Evaluation of changes in the microscopic physical structures in plastic during molding is possible by multifaceted measurements using general-purpose instruments. It is possible to understand the physical properties of plastics and the factors that influence those properties. Multifaceted Evaluation of Changes in Physical Properties of Recycled Plastics by Advanced Recycling Process and Influencing Microstructural Changes (Part 2): Example of Application to Simulated Degraded Polypropylene AGX -V2 AUTOGRAPH Precision Universal Testing Machine HITS -TX High Speed Tensile Testing Machine DUH -210 Dynamic Ultra Micro Hardness Tester DSC-60 Plus Differential Scanning Calorimeter SPM-Nanoa Scanning Probe Microscope AIRsight Infrared and Raman Microscope Karen Maruyama 1 , Xu Yan 1 , Motofumi Kimura 1 , Masato Hirade 1 , Mitsuru Ohta 1 , Zen Miyazaki 1 , Shigeru Yao 2 1 Shimadzu Corporation, 2 Fukuoka University Test piece shape Evaluations conducted ISO 527-2 1A Tensile test, hardness test, DSC, FTIR, SPM ASTM D1822 TYPE L High speed tensile test (The test pieces used in DSC, FTIR and SPM were cut and processed to the corresponding size and state.) First, in order to confirm the effects of the advanced recycling process on the physical properties of the plastic, strain at break and the elastic modulus of the samples were investigated by a static tensile test, and the impact property was investigated by a high speed tensile test. Next, to discuss the factors in changes in the strain at break and impact property, the following evaluations were conducted. • Dynamic ultra micro hardness tester (DUH): Hardness • Differential scanning calorimeter (DSC): Crystallization start temperature • Scanning probe microscope (SPM): Orientation • Fourier transform infrared spectrophotometer (FTIR): Ratio of helical structure and parallel structure Evaluations The tensile test was conducted using the Autograph precision universal testing machine. A TRViewX non-contact digital video extensometer was used as the extensometer. Fig. 1 shows the appearance of the testing machine, Fig. 2 shows the appearance during a test, and Table 2 shows the instrument configuration and test conditions. Fig. 3 shows the stress-strain curves to break, Fig. 4 shows the stress-strain curves in the elastic region, and Table 3 shows the measured results of the strain at break. Strain at break increased in the test pieces with the advanced recycling process in comparison with those without the process. Table 4 shows the measured results of the elastic modulus. The elastic modulus with the advanced recycling process was lower than that without the process. Evaluation of Strain at Break and Elastic Modulus by Tensile Test Fig. 2 Appearance during Test Instrument : AGX-V2 Load cell : 5 kN Grip : Pneumatic flat grip Extensometer : TRViewX 500D Software : TRAPEZIUM X-V Test speed : 1 mm/min (measurement of elastic modulus) 50 mm/min (measurement to break) Gauge length : 75 mm Number of tests : n = 7 Test piece width : 10 mm Test piece thickness : 4 mm Grip distance : 115 mm Stroke strain (%) Stress (Mpa) Stroke strain (%) Stress (Mpa) Displacement gauge strain (%) Stress (Mpa) Displacement gauge strain (%) Stress (Mpa) Fig. 4 Stress-Strain Curves in Elastic Region (Left: With Advanced Recycling Process, Right: Without Advanced Recycling Process) Fig. 3 Stress-Strain Curves to Break (Left: With Advanced Recycling Process, Right: Without Advanced Recycling Process)
Application News Fig. 5 HITS-TX Evaluation of Impact Property by High Speed Tensile Test Table 3 Measured Results of Strain at Break Next, the high speed tensile test was conducted using the high speed tensile testing machine (HITS-TX). Fig. 5 shows the appearance of the instrument, Table 5 shows the instrument configuration and test conditions, and Fig. 6 shows the stress- strain curves. Table 6 and Table 7 show the measured results of strain at break with and without the advanced recycling process, respectively. As in the static test, in comparison with the results without the advanced recycling process, the strain at break with the advanced recycling process increased in the high speed tensile test, and the break energy also increased. Test piece Strain at break (%) W/o Advanced recycling process_1 448.1 W/o Advanced recycling process_2 676.0 W/o Advanced recycling process_3 579.6 W/o Advanced recycling process_4 612.3 W/o Advanced recycling process_5 586.8 W/o Advanced recycling process_6 638.3 W/o Advanced recycling process_7 449.8 Average 570.1 Standard deviation 88.86 Coefficient of variation 15.6 % Test piece Strain at break (%) W/ Advanced recycling process_1 594.1 W/ Advanced recycling process_2 622.5 W/ Advanced recycling process_3 673.2 W/ Advanced recycling process_4 599.2 W/ Advanced recycling process_5 539.8 W/ Advanced recycling process_6 578.0 W/ Advanced recycling process_7 604.9 Average 601.7 Standard deviation 40.85 Coefficient of variation 6.8 % Test piece Elastic modulus (MPa) W/o Advanced recycling process_1 1622 W/o Advanced recycling process_2 1642 W/o Advanced recycling process_3 1613 W/o Advanced recycling process_4 1668 W/o Advanced recycling process_5 1625 W/o Advanced recycling process_6 1653 W/o Advanced recycling process_7 1723 Average 1649 Standard deviation 37.64 Coefficient of variation 2.3 % Test piece Elastic modulus (MPa) W/ Advanced recycling process_1 1551 W/ Advanced recycling process_2 1603 W/ Advanced recycling process_3 1618 W/ Advanced recycling process_4 1658 W/ Advanced recycling process_5 1652 W/ Advanced recycling process_6 1593 W/ Advanced recycling process_7 1610 Average 1612 Standard deviation 36.33 Coefficient of variation 2.3 % Table 4 Measured Results of Elastic Modulus Table 5 Instrument Configuration and Test Conditions Instrument : HITS-TX Load cell : 10 kN Grip : Flat grip for high speed tensile test Extensometer : Chuck displacement gauge Software : TRAPEZIUM HITS Test speed : 10, 1/s Number of tests : n = 5 Grip distance : 40 mm Stress (MPa) Stress (MPa) With process Without process Chuck displacement strain (%) Chuck displacement strain (%) Fig. 6 Stress-Strain Curves to Break (Top: With Advanced Recycling Process, Bottom: Without Advanced Recycling Process) Table 6 Measured Results of Strain at Break with Advanced Recycling Process (Average of N = 5) Strain rate (/s) Yield stress (MPa) Strain at break (%) Break energy(J) 100 Average 53.327 57.006 2.335 Standard deviation 0.541 2.075 0.086 Coefficient of variation (%) 1 3.6 0.037 10 Average 48.158 59.747 2.105 Standard deviation 098 1.239 0.042 Coefficient of variation (%) 0.2 2 0.020 Table 7 Measured Results of Strain at Break without Advanced Recycling Process (Average of N = 5) Strain rate (/s) Yield stress (MPa) Strain at break (%) Break energy(J) 100 Average 53.814 55.286 2.297 Standard deviation 0.493 2.649 0.097 Coefficient of variation (%) 0.92 4.8 0.042 10 Average 48.636 56.639 2.051 Standard deviation 0.028 3.523 0.123 Coefficient of variation (%) 0.5 6.2 0.060 The hardness test was conducted using the dynamic ultra micro hardness tester (DUH). The test was carried out near the center of the parallel part of the ISO 527-2 1A test pieces. Fig. 7 shows the appearance of the instrument. Table 8 shows the test conditions, Fig. 8 shows the test force-indentation depth curves, and Table 9 shows the measured results of the indentation hardness H IT . The H IT with the advanced recycling process was lower than that without the process. Hardness Evaluation Fig. 7 DUH -210 Table 8 Test Conditions Instrument : DUH-210 Indenter : Berkovich indenter Test mode : Load/unload test Test force : 20 mN Loading/unloading time : 30 s Load holding time : 40 s Number of tests : 10 Room temperature : 23 ± 2 ˚C Humidity : 50 ± 10 % Test force (mN) Indentation depth (µm) Test force (mN) Indentation depth (µm) Fig. 8 Test Force-Indentation Depth Curves (Left: With Advanced Recycling Process, Right: Without Advanced Recycling Process) Table 9 Measured Results of Indentation Hardness H IT (N = 10) Test piece HIT Average (MPa) Standard deviation Coefficient of variation (%) With advanced recycling process 70.3 2.1 3.0 Without advanced recycling process 74.0 1.9 2.6 Evaluation of Crystallization Start Temperature by Thermal Analysis This section presents the results of measurements with the differential scanning calorimeter (DSC). Because a difference was observed in the crystallization process during cooling, the results with and without the advanced recycling process were compared, focusing on the crystallization start temperature. Fig. 9 shows the appearance of the instrument. Table 10 shows the measurement conditions, Fig. 10 shows representative DSC curves during cooling after heating (blue line: with advanced recycling process, red line: without advanced recycling process), and Table 11 shows the measured results of the crystallization start temperature. With the advanced recycling process, the crystallization start temperature was lower than that without the process. The cause of this difference is considered to be a delay in crystallization because the motion of molecule chains was suppressed by an increase in polymer entanglements due to the heat treatment in the advanced recycling process. Although not shown here, the heat of fusion in the heating process was compared, but no significant difference could be seen in the degree of crystallization with and without the advanced recycling process.
Application News Helical structure 998 cm -1 Parallel structure 971 cm -1 With process_cross section Without process_cross section 100.00 110.00 120.00 130.00 140.00 Temp [゚C] -0.00 10.00 20.00 mW DSC 122.14 ゚C 121.56 ゚C 青:高度再生処理有 赤:高度再生処理無 Blue: With advanced recycling process Red: Without advanced recycling process Fig. 9 DSC-60Plus Evaluation of Ratio of Polymer Structures by FTIR The polymer structures of PP are the helical structure and the parallel structure, and it is possible to detect the peaks originating from these structures by using FTIR. Here, the difference in the ratio of these two structures with and without the advanced recycling process was evaluated. Test slices with a thickness of 15 μm were taken from the parallel part of the ISO 527-2 1A test pieces with a microtome, and area mapping measurements by the transmission method were carried out using the infrared mode of the AIRsight infrared and Raman microscope. Fig. 13 shows the appearance of the instrument and Table 12 shows the measurement conditions. Fig. 11 shows spectra of both the samples with and without the advanced recycling process at each point. Peaks originating from the helical structure at 998 cm -1 and from the parallel structure at 971 cm -1 were confirmed, and chemical images were prepared based on the height ratio (helical/parallel) of these two peaks in the samples with and without the advanced recycling process, as shown in Fig. 12. For comparison, the vertical axes of the chemical images were unified at 0.78 to 0.84 AU. The results confirmed that the sample with the advanced recycling process has a higher in-plane average value of the helical/parallel ratio than the sample without the advanced recycling process. The difference in orientation with and without the advanced recycling process was evaluated. With SPM, it is possible to measure the distribution of diverse physical quantities according to the selection of the measurement mode, and micron-level regions can be evaluated. Here, the adhesion distribution was used, as this is effective for evaluating the uniformity of a sample. Cross sections of the parallel part of the ISO 527-2 1A test pieces were taken with a cryomicrotome, and the cross sections were measured using the SPM. Fig. 14 shows the appearance of the instrument, and Table 13 shows the measurement conditions. Fig. 15 and Fig. 16 show the topography images and adhesion images with and without the advanced recycling process, respectively. Without the advanced recycling process, a striped structure could be observed in the adhesion image with a 1 μm field of view, which is the micron-level region. This striped structure is considered to indicate orientation, and is thought to show the effect of shearing in the molding process. On the other hand, with the advanced recycling process, a uniform distribution can be seen in the field of view, suggesting that the effect of shearing is moderated by the advanced recycling process. Evaluation of Orientation by SPM Fig. 14 SPM-Nanoa Table 10 Measurement Conditions Instrument : DSC-60Plus Heating/cooling rate : 10 ˚C/min Sample amount : 6 mg Atmosphere : Nitrogen Fig. 10 DSC Curves for Crystallization (Cooling Process) Table 11 Measured Results of Crystallization Start Temperature (N = 5) Test piece Crystallization start temperature (˚C) Average Standard deviation With advanced recycling process 121.64 0.067 Without advanced recycling process 122.06 0.117 Based on the two points that (1) differences in mechanical properties were observed with and without the advanced recycling process, and (2) entanglements of polymers are thought to increase due to a decrease in the crystallization start temperature, which is one thermal property, it is conceivable that the microscopic physical structures in the plastic may change as a result of the advanced recycling process. Therefore, in evaluating the changes in the microscopic physical structures, this study focused on the proportion of the helical structure to the parallel structure and orientation, which is closely related to polymer entanglements. Table 12 Measurement Conditions Instruments : IRXross , AIRsight (infrared mode) Resolution : 8 cm -1 Accumulation : 10 times Apodization function : SqrTriangle Aperture size : 30 μm × 30 μm Step width : 30 μm Mapping range : 330 μm × 270 μm Detector : T2SL Fig. 11 Infrared Spectra of Samples with/without Advanced Recycling Process Fig. 12 Chemical Images of Test Slices (Left: With Advanced Recycling Process, Right: Without Advanced Recycling Process) Fig. 13 IRXross and AIRsight Table 13 Measurement Conditions Instrument : SPM-Nanoa Scanner : Medium-range scanner (XY: 30 μm, Z: 5 μm) Observation mode : Nano 3D Mapping Fast Observation field of view : 1 μm × 1 μm Pixel : 256 × 256 Fig. 15 Topography Image and Adhesion Image with Advanced Recycling Process 1 μm field of view Topography image Adhesion image 1 μm field of view Fig. 16 Topography Image and Adhesion Image without Advanced Recycling Process 1 μm field of view Topography image Adhesion image 1 μm field of view
Application News www.shimadzu.com/an/ Shimadzu Corporation © Shimadzu Corporation, 2025 For Research Use Only. Not for use in diagnostic procedures. This publication may contain references to products that are not available in your country. Please contact us to check the availability of these products in your country. The content of this publication shall not be reproduced, altered or sold for any commercial purpose without the written approval of Shimadzu. See http://www.shimadzu.com/about/trademarks/index.html for details. Third party trademarks and trade names may be used in this publication to refer to either the entities or their products/services, whether or not they are used with trademark symbol “TM” or “”. Shimadzu disclaims any proprietary interest in trademarks and trade names other than its own. The information contained herein is provided to you "as is" without warranty of any kind including without limitation warranties as to its accuracy or completeness. Shimadzu does not assume any responsibility or liability for any damage, whether direct or indirect, relating to the use of this publication. This publication is based upon the information available to Shimadzu on or before the date of publication, and subject to change without notice. First Edition: Jul. 2025 01-00868-EN Study of Changes in Microscopic Physical Structure by Multifaceted Evaluation DUH, AGX, HITS, TRAPEZIUM, IRXross, AIRsight, SPM-Nanoa, and Nano 3D Mapping are trademarks of Shimadzu Corporation or its affiliated companies in Japan and/or other countries. (1) Verification of increase in tie molecules and an intermediate layers from the macro viewpoint First, this section considers the existence of intermediate layers containing tie molecules, which are expected to have a strong influence on the improvement of the impact property and strain at break of plastics. Both the elastic modulus and H IT were reduced by the advanced recycling process. The cause of this change is considered to be either a decrease in the degree of crystallization, or an increase in the intermediate layers containing tie molecules. In this evaluation, the DSC analysis showed that there was no difference in the heat of fusion, confirming that there is no difference in the degree of crystallization with and without the advanced recycling process. Based on these facts, it can be thought that the intermediate layers containing tie molecules are increased by the advanced recycling process. The image of the tie molecules and intermediate layers is shown in Fig.17. (2) Consideration of changes in the physical structure from the micro viewpoint In the section, the increase in tie molecules is considered, changing the perspective from the macroscopic physical properties of the elastic modulus, H IT , and the degree of crystallization to the microscopic viewpoint. It is suggested that the increase in polymer entanglements during melting in the advanced recycling process contributes to the formation of intermediate layers containing tie molecules. The condition of polymer entanglements during melting is estimated from the polymer structure in the solid state after molding. In the molding process from the molten state, it is thought that the polymer is elongated to the parallel structure when shearing is applied, and the probability that the polymer will become a helical structure increases as polymer relaxation proceeds. When the ratio of the parallel structure and the helical structure was investigated by FTIR, it was found that the helical structures had increased. Based on this, it is thought that relaxation proceeds as a result of the advanced recycling process. Moreover, the evaluation of the orientation in the micro region by SPM showed that the distribution becomes more uniform as a result of the advanced recycling process, which also supports the conclusion that the effect of shearing was moderated by the advanced recycling process. As mentioned previously, the crystallization start temperature during cooling in the DSC measurements decreased as a result of the advanced recycling process, which also suggests that polymer entanglements increased. Based on the multifaceted evaluation described above, it is though that relaxation of the polymer during melting was promoted by the advanced recycling process, leading to an increase in polymer entanglements and an accompanying increase in the intermediate layers containing tie molecules, and as a result, the impact property and strain at break of the recycled plastic improved. <Reference> 1) Present and future of waste plastics: plastic resource circulation in sustainable society, The Japan Institute of Energy, p. 147 <Acknowledgement> The authors wish to express their heartfelt gratitude to Mr. Kaga, Mr. Fujioka, and Mr. Hisaizumi of ISONO Co., Ltd. for their guidance in the preparation of this report. Conclusion It was found that the impact property and strain at break of PP were improved by the advanced recycling process. This study also demonstrated that the multifaceted evaluation described in this article is an effective tool for evaluating changes in the microscopic physical structure. Reference: Image of Entaglements during Melting of Polymers and Crystal Structure after Cooling 1) As reference, the following diagram shows the image of the aggregation state of polymers explained in the main text. If entanglements of the molecules are increased by heat treatment in the advanced recycling process, the number of tie molecules after crystallization will increase. Crystals Molten condition Few polymer entanglements Many polymer entanglements Cooling Many intermediate layers with tie molecules Few tie molecules With advanced recycling process Without advanced recycling process Fig. 17 Image of Aggregation State of Polymers
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