Abstract A fragmentation model based on global load sharing (GLS) theory is developed to obtain stress-strain curves that describe the mechanical behavior of unidirectional composites. The model is named C N B + τ * because it is based on the Critical Number of Breaks model (CNB) and on the correction of the fiber matrix interfacial strength, τ *. Model allows both obtaining the ultimate tensile strength of CFRP and GFRP composites, and correcting the σ vs ε curve to match its peak point with the predicted strength, which is more accurate than the one obtained by previous GLS-based models. Our model is used to classify the mechanical response of the material according to the energetic contributions of two phenomena up to the failure: intact fibers (IF) and fragmentation (FM). Additionally, the influence of fiber content, V f, on the tensile strength, σ U, failure strain, ε U, and total strain energy, U T, is analyzed by means of novel mechanical-performance maps obtained by the model. The maps show a dissimilar behavior of σ U, ε U and U T with V f between GFRP and CFRP composites. The low influence of V f on the percent energetic contributions of IF and FM zones, as well as the larger energetic contribution of the FM zone, are common conclusions that can be addressed for both kinds of composites.

explaining Stress vs. strain behavior of carbon composite with a nano mat of PAN-derived carbon fiber at the top of assembly.

Raw data of tensile stress-strain curves at 25 ℃ and 170 ℃ of unsized SCF/PEI and CNT-PDA@SCF/PEI composites; Raw data of tensile stress-strain curves at 25 ℃ of PEI with different CTC numbers.; Raw data of tensile stress-strain curves at 25 ℃ of PEI with CTC, TC and CC treatments Raw data of tensile stress-strain curves at 170 ℃ of PEI before and after the CTC treatment.

Stress-strain curves of uniaxial tension test subjected to quasi-static axial loads of RTV-2 material. Please refer to "E-Skin Development and Prototyping via Soft Tooling and Composites with Silicone Rubber and Carbon Nanotubes" on Materials (MDPI) for details.

True stress–strain data from specimen mechanical tests, XRD results, and constitutive model code.

This dataset comprises the raw and processed data generated during the development and testing of starch-gelatin bio-composites, specifically including: 1) stress-strain curve data; 2) weight loss records from soil burial degradation tests; 3) statistical data on seed germination rates. These data directly support the findings presented in Figures 11-16 of the manuscript titled "A synthetic approach and basic performance study of bio-based composite materials based on starch and gelatin as matrix phase examples: Application to sustainable toy design".

In this dataset, cooling-rate-dependent properties of polyphenylene sulfide (PPS) and carbon fiber reinforced PPS (CF/PPS) manufactured with different cooling rates (1, 5, and 10 °C/min) are included. Cooling-rate-dependent thermal properties (crystallization temperature, glass transition temperature, melting temperature, and coefficients of thermal expansion), physical properties (crystallinity and density), mechanical properties (moduli, yield stress, ultimate stress, and stress–strain curves), and fracture properties (load–displacement curves and R-curves) are presented. Detailed information are presented in a research article linked to this dataset. "summary-of-all-data.xlsx": Summary of all data "PPS-tensile-stress-strain-curves.xlsx": Tensile stress–strain curves of neat PPS "PPS-compressive-stress-strain-curves.xlsx": Compressive stress–strain curves of neat PPS "PPS-shear-stress-strain-curves.xlsx": Shear stress–strain curves of neat PPS "CFPPS-shear-stress-strain-curves.xlsx": Shear stress–strain curves of CF/PPS "CFPPS-transverse-stress-strain-curves.xlsx": Transverse tensile stress–strain curves of CF/PPS "CFPPS-DCB-curves.xlsx": Load–displacement curves and R-curves of DCB (mode I fracture toughness) tests "CFPPS-ENF-curves.xlsx": Load–displacement curves and R-curves of ENF (mode II fracture toughness) tests

Particle size distribution data measured by dynamic light scattering for coarse glass powder and fine (attritor milled) glass powder (Fig02). Contains Microsoft Excel .xlsx files and .txt files with particle size distributions, as well as script and data files for generating plots (.txt). Raw SEM images (.tif) of coarse and fine glass powder are also included. Results from X-ray micro-computed tomography 3D object analysis (Fig03) are supplied in Microsoft Excel .xlsx files. For composites made using films and precipitate, three volumes of interest (VOIs) are shown in separate .xlsx files. Object analysis results are combined into one .xlsx files for each composite condition to generate an average object size distribution, which is exported to a .txt file. μCT slice images and SEM images of composites fabricated from composite films and precipitate are also included in .png format. Script files for generating figures are also included (.txt). Mechanical testing data from tensile tests of composites fabricated from composite films and precipitate (Fig04). Tests were carried out in 37°C water. Contains .txt files with example stress-strain curves, as well as script and data files for generating plots (.txt). Digital photographs (.png files) of samples before and after tensile failure are also included. Plots are generated using gnuplot (www.gnuplot.info),

This dataset contains raw test data for TPU/BC/CFF composite samples, which were used in the study titled "Flexible Bio-Composites with Continuous Natural Fibre and Bamboo Charcoal: Supreme Flame Retardancy, Mechanical Resilience, Energy-Absorbing & Printability Performance" (in preparation). The Excel file includes the measured stress–strain values, test parameters, and plotted diagrams for each tested specimen. The data were obtained using standard uniaxial tensile testing procedures at room temperature.

In our study, we investigated the effects of the silver-coated graphene (Ag@GNS) content on the microstructural and mechanical properties of Ti-13Nb-13Zr (TC26) based composites and explored their fracture mechanisms. The results showed that with an increase in Ag@GNS content, the in situ-generated TiC aggregated in the grain boundaries, which led to a decrease in α grain size and an increase in the dislocation density. Meanwhile, the density, 0.2% yield strength and ultimate tensile strength exhibited an initial increase followed by a decrease. When the Ag@GNS content achieved 0.5 wt.%, the TC26 based composites demonstrated the best mechanical performance with the hardness of 387.87 HV0.1, 0.2% yield strength of 950.54 MPa and tensile strength of 1169.46 MPa, respectively, where the elongation maintained 6.49%. Moreover, the elastic modulus of 0.5Ag@GNS/TC26 composite was 28.30 GPa, which meets the requirements of the elastic modulus of human implants. The tensile strength of the composites was affected by the contents of the reinforcing phases, TiC and Ti3Ag at the interface. Both excessive and insufficient reinforcing phases deteriorate tensile strength. Therefore, these uploaded figures come from the results of above study. Figure 1 shows the Schematic diagram of Ag@GNS/TC26 composites prepared by SLM. Figure 2 shows the SEM images of titanium matrix composite powders with different Ag@GNS contents. (a) 0.3 wt.% Ag@GNS, (b) 0.5 wt.% Ag@GNS, (c) 0.7 wt.% Ag@GNS, (d) 0.9 wt.% Ag@GNSFigure 3 shows the XRD patterns of titanium matrix composites with different Ag@GNS contents. (a) XRD patterns of titanium matrix composites with different Ag@GNS contents, (b) Enlarged view of areas 37°-42°Figure 4 shows the OM images of titanium matrix composites with different Ag@GNS contents. (a) 0.3Ag@GNS/TC26 composite, (b) 0.5Ag@GNS/TC26 composite, (c) 0.7Ag@GNS/TC26 composite, (d) 0.9Ag@GNS/TC26 compositeFigure 5 shows the SEM images of titanium matrix composites with different Ag@GNS content. (a-c) 0.3Ag@GNS/TC26 composite, (d-f) 0.5Ag@GNS/TC26 composite, (g-i) 0.7Ag@GNS/TC26 composite, (j-l) 0.9Ag@GNS/TC26 compositeFigure 6 shows the Measured density of titanium matrix composites with different Ag@GNS contents.Figure 7 shows the TEM, HRTEM and GPA images of 0.5Ag@GNS/TC26 composite. (a) Bright-field TEM image of 0.5Ag@GNS/TC26 composite, (b) Enlarged view of the yellow box in Fig. 7(a), (c) HRTEM image in yellow box in Fig. 7(b), (d) corresponding GPA image in Fig. 7(c).Figure 8 shows the Contrast, inverse polarity plots and grain size histograms of titanium matrix composites with different Ag@GNS contents. (a1-a3) 0.3Ag@GNS/TC26 composite, (b1-b3) 0.5Ag@GNS/TC26 composite, (c1-c3) 0.7Ag@GNS/TC26 composite, (d1-d3) 0.9Ag@GNS/TC26 composite.Figure 9 shows the KAM diagrams of titanium matrix composites with different Ag@GNS contents. (a1, a2) 0.3Ag@GNS/TC26 composite, (b1, b2) 0.5Ag@GNS/TC26 composite, (c1, c2) 0.7Ag@GNS/TC26 composite, (d1, d2) 0.9Ag@GNS/TC26 compositeFigure 10 shows the High-angle and low-angle grain boundaries distribution of titanium matrix composites with different Ag@GNS content. (a) 0.3Ag@GNS/TC26 composite, (b) 0.5Ag@GNS/TC26 composite, (c) 0.7Ag@GNS/TC26 composite, (d) 0.9 Ag@GNS/TC26 compositeFigure 11 shows the Parametric properties of composites. (a) hardness diagram, (b) stress-strain curve diagram, (c) reported properties of titanium matrix composites [9, 34, 43-47]Figure 12 shows the Fracture morphology of titanium matrix composites with different Ag@GNS contents. (a) 0.3Ag@GNS/TC26 composite, (b) 0.5Ag@GNS/TC26 composite, (c) 0.7Ag@GNS/TC26 composite, (d) 0.9 Ag@GNS/TC26 compositeFigure 13 shows the Schematic diagram of the tensile process of titanium matrix composites with different Ag@GNS content.

A new method has been developed for creating localised in-plane fibre-waviness in composite coupons and used to create a large batch of specimens. This method could be used by manufacturers to experimentally explore the effect of fibre-waviness on composite structures both directly and indirectly to develop and validate computational models. The specimens were assessed using ultrasound, digital image correlation and a novel inspection technique capable of measuring residual strain fields. To explore how the defect affects the performance of composite structures, the specimens were then loaded to failure. Predictions of remnant strength were made using a simple ultrasound damage metric and a new residual strain-based damage metric. The predictions made using residual strain measurements were found to be substantially more effective at characterising ultimate strength than ultrasound measurements. This suggests that residual strains have a significant effect on the failure of laminates co...

Overcoming the strength–ductility trade-off remains a central challenge for titanium matrix composites, because ceramic reinforcements often induce severe interfacial stress concentration and premature cracking. Here, we develop a hierarchical heterostructure in Ti–6.5Al–2Zr–1Mo–1 V through in-situ reaction and subsequent hot extrusion, consisting of nanoscale TiB reinforcements, primary α, β phase and secondary α. The pronounced hetero-deformation-induced strengthening and activation of ⟨c + a⟩ dislocations enable the composite to achieve 1351 MPa tensile strength and 15.9% elongation, representing increases of 40.1% and 26.2% over the matrix alloy, respectively. This strategy offers a scalable route for designing high-performance titanium composites. Highlightsαp, β, autocatalytic αs and in-situ-formed nanoscale TiB jointly constitute the HHS composite.The HHS delivers 1351 MPa tensile strength and 15.9% elongation.Multiple deformation mechanisms collectively sustain the work-hardening capacity.TiB-assisted strain accommodation alleviates local stress concentration. αp, β, autocatalytic αs and in-situ-formed nanoscale TiB jointly constitute the HHS composite. The HHS delivers 1351 MPa tensile strength and 15.9% elongation. Multiple deformation mechanisms collectively sustain the work-hardening capacity. TiB-assisted strain accommodation alleviates local stress concentration.

Thermal data measured by DSC for composites of PLLA and PLLA:PLCL(70:30)-with P45Ca45 and P40Ca50 phosphate glass, before degradation (Fig01). Contains Microsoft Excel file with Tg measurements and experimental details. Script and data files for generating plots are also given (.txt). Representative stress-strain curves (Fig02) from tensile tests of composites in ambient conditions (t0dry) and immersed in 37°C water (t0wet), all before degradation. Contains .txt files with example stress-strain curves, as well as script and data files for generating plots (.txt). Also contains Microsoft Excel file with measured mechanical properties, and key to identifying stress-strain curves (.xlsx). Calculation of mechanical properties of composites in ambient conditions (t0dry) and immersed in 37°C water (t0wet), all before degradation (Fig03). Fig03_modulus.xlsx contains calculation of predicted modulus from Counto model, and analysis of the goodness-of-fit. Voigt-Reuss bounds are also calculated for plotting in Fig 3. Fig03_yieldstrength.xlsx contains calculation of the predicted lower bound yield strength, as well as conversion of glass weight fractions to volume fractions used for plotting. Script and data files for generating plots are also given (.txt). Measurements from long-term degradation tests of composites in 37°C phosphate-buffered saline. Contains Microsoft Excel file (Fig04_data.xlsx) with raw pH, Ca²⁺ electrode potential, and wet mass measurements, along with calculation of Ca²⁺ concentration and wet mass %, along with appropriate averages and standard deviations. Example Ca²⁺ ISE calibration curve is also shown. Script and data files for generating plots are also given (.txt). Measurements of composite sample mass before and after 5, 30, and 120 days degradation in 37°C phosphate-buffered saline. Microsoft Excel file (Fig05_composite_mass.xlsx) with wet mass, dry mass, and ash content measurements, as well as calculations of water, glass, and polymer mass percentages. Fig05_data_export.xlsx contains data from the previous file, rearranged for plotting over time. Script and data files for generating plots are also given (.txt). X-ray diffraction data for polymer crystallisation within composites (Fig06.xlsx). Raw XRD patterns (.uxd) given for examples of samples undergoing no polymer crystallisation, and extensive polymer crystallisation. Polymer crystallinity percentage measured by XRD is also given, normalised to the proportion of polymer present in the composite. Script and data files for generating plots are also given (.txt). DSC data showing enthalpy relaxation (Fig07) occurring during degradation is given in a Microsoft Excel file. Example raw DSC curves before and after degradation are supplied, as well as the change in enthalpy relaxation after 5, 30, and 120 days degradation. Script and data files for generating plots are also given (.txt). Raw SEM images of selected compositions before and after 120 days degradation (Fig08) are given (.tif), along with example XRD pattern showing the inorganic phases present within composite materials after degradation (.uxd). Script and data files for generating plots are also given (.txt), as well as illustration file (.svg) and figure (.png). Mechanical properties (modulus, yield strength, elongation at break) measured in 37°C water before and after 5, 30, and 120 days degradation in 37°C phosphate-buffered saline (Fig09). Microsoft Excel file (.xlsx) given with data for each timepoint, as well as script and data files for generating plots are also given (.txt). Raw ashing data (Tab01) showing sample masses for as-fabricated composites. Experimental details, measurements (slide mass before and after ashing), and ash calculations given in Microsoft Excel file (.xlsx). Plots are generated using gnuplot (www.gnuplot.info), Note: In raw data, deprecated glass codes are sometimes used. PG7 denotes glass code P45Ca45 (P₂O₅)₄₅(CaO)₄₅(Na₂O)₁₀, and PG11 denotes glass code P40Ca50 (P₂O₅)₄₀(CaO)₅₀(Na₂O)₁₀.

Single fiber test data and SEM scan behind the publications

Kumar, R., L.P. Mikkelsen, H. Lilholt, B. Madsen, Understanding the mechanical response of glass and carbon fibres: stress-strain analysis and modulus determination IOP Conf. Ser.: Mater. Sci. Eng. 942, 012033, https://doi.org/10.1088/1757-899X/942/1/012033, 2020

Rajnish Kumar, Lars P Mikkelsen, Hans Lilholt and Bo Madsen, Experimental Method for Tensile Testing of Unidirectional Carbon Fibre Composites Using Improved Specimen Type and Data Analysis, Materials, 14, 3939, https://doi.org/10.3390/ma14143939, 2021.

and

Rajnish Kumar, Lars P Mikkelsen, Hans Lilholt and Bo Madsen, Weibull parameters determined from a comprehensive dataset of tensile testing fo single carbon fibers, Submitted, 2024

to where a reference should be given.

A video describing the test-setup can be found in the following link: https://panopto.dtu.dk/Panopto/Pages/Viewer.aspx?id=50c10945-0612-4126-9e99-b00700cfbaf2&start=0

The data-set cover single fiber test of a carbon and glass fiber in the gauge section range from 20-80 mm for carbon fiber and from 40-80 mm for glass fiber. There are three files for each gauge-section:

... Data.xslx: The individual tensile curves with one sheet for each fiber. There are around 150 fibers in each set

... Results.xslx: One excel-sheet containing a summary of the parameters obtained for the individual fibers.

....Figures.doc: Word file showing a plot of the graphs

In addition to this, there are for the carbon and glass fiber case a test setup complience calculation saved in the

.... Compliance.xslx excel-sheet

and SEM scans of a large approximately 2x20 mm cross-section of a pultruded profile based on the carbon fibers. This scan can be used for validating the fiber diameter distribution found in the single fiber testing. The SEM scan is saved in the

Carbon_HyFisyn... files

This set of files also include a matlab file (.m) which are used for determine the fiber volume fraction of the composite.

Scripts to plot and analysing the data can be found on the following places:

Google Colab: https://colab.research.google.com/drive/1GdmRGOuy6SUuRXdbbyxemczgAUZl8JaM?usp=sharing

Code Ocean: Lars P. Mikkelsen, Rajnish Kumar (2022) Understanding the mechanical response of glass and carbon fibres: stress-strain analysis and modulus determination [Source Code]. https://doi.org/10.24433/CO.5998905.v1

Dynamic tensile test data from experiments conducted on carbon fiber epoxy AP-PLY composites. A paper with a complete description of the data collection process is under review. This description will be updated with a link to the paper in due time.

RESEARCH AIMS Quasi-isotropic [0, 45, 90, -45]4S and cross-ply [0, 90]12S laminates with conventional or AP-PLY configurations were tested to failure under dynamic tensile loading using a split-Hopkinson bar, to investigate the effect of the AP-PLY architecture on the in-plane mechanical properties of the laminates (specifically longitudinal modulus and strength).

TESTING PROCEDURE Laminates were manufactured using SHD Composites VTC401 unidirectional prepregs (VTC401-UD300-T700-24K-36%RW-600P SHD1579-600P). Laminates were laid up by hand, and subsequently cured in a hot press at 110 degrees centigrade at a pressure of 4 bar. Dogbone shaped specimens were extracted using CNC milling. Four holes were drilled into the ends of each specimen to allow them to be clamped in the split-Hopkinson bar grips. Aluminium end tabs were adhered to the specimens using epoxy adhesives (Araldite 2021 and Permabond ET5428). Specimens dimensions are illustrated in the "specimen_dimensions.pdf" included with the data.

Testing was conducted at the European Commission's Joint Research Center, specifically, the European Lab for Structural Analysis HopLab (https://joint-research-centre.ec.europa.eu/laboratories-and-facilities/european-laboratory-structural-assessment-large-hopkinson-bar-facility-elsa-hoplab_en). Specimens were loaded to failure at strain rates of ~30s-1 using an extremely large split Hopkinson bar. Strains were recorded using 2D digital image correlation, forces were obtained from transducers in the SHB.

DATA FORMAT Data is provided in .csv format. "QI" is used to indicate a quasi-isotropic laminate with 0, 45, 90, and -45 degree fiber orientations. "XP" denotes cross-ply laminates containing only 0 and 90 degree plies. Filenames containing "_AP_PLY" refer to specimens with an AP-PLY quasi-woven internal architecture. Filenames containing "_BASE" refer to baseline, non AP-PLY specimens.

Column headings are: index (-), Time (s), Strain (-), Stress (MPa)

This dataset supports the manuscript entitled “Strain-rate-dependent tensile behaviour of additively manufactured continuous carbon fibre-reinforced Onyx composites”. The files include raw and processed tensile test data for neat Onyx and continuous carbon fibre-reinforced Onyx composites (CFF/Onyx) tested at strain rates of 4.2 × 10⁻⁴ s⁻¹, 1 s⁻¹ and 100 s⁻¹. The raw data contain the original experimental and calculated stress and strain data, while the processed data contain the stress and strain data tested at the strain rate of 100 s⁻¹ after the Fast Fourier Transform (FFT) and Adjacent Averaging (AAv) tool in OriginPro for plotting smooth stress-strain curves under dynamic tensile testing.

In this research, we bridge theory and experiment by developing an integrated framework that couples in situ chemical strain measurements with mechanics modeling to quantify stress and strain energy evolution during ion insertion/extraction.

This data article presents four experiment results related to flax fibre composites with epoxy shape memory polymer matrix: water vapor absorption, mass diffusion immersed in water, hygroscopic expansion, mechanical properties. The water vapor absorption tests are described by raw data related to four types of laminates with weights measured at different relative humidity (0%, 9%, 33%, 44%,75%, 85% and 100%). The mass diffusion experiments are related to weights of immersed samples over time. The unidirectional composite hygroscopic expansion is also measured along the fibre longitude and transverse directions. The, mechanical properties of flax composite at various temperatures (20°C, 40°C, 60°C, 80°C and 100°C) and humidity environments (50% and immersed) are also described. Load-displacement diagrams of the hygromorph composites are converted into stress-strain diagrams via a compliance calibration, from which the tensile moduli are extracted. The data presented in this article can provide a benchmark for the development of new models, or for the determination of other properties via post processing.

In the "design-simulation-preparation-characterization" research framework for carbon nanomaterial-reinforced polyvinyl alcohol (PVA) composite fibers, molecular dynamics (MD) simulations play a core role. Using Materials Studio 2023 and LAMMPS, oriented composite models of carbon nanotubes (CNT), graphene (GN) with PVA, along with pure PVA control models, were constructed. Simulations included geometric optimization, NPT dynamic processes, and annealing treatments, followed by calculations of mechanical properties (Young's modulus, shear modulus, density) and Z-direction stress-strain curves. Confined shear simulations mimicked shear-stretching in wet spinning, with relative concentration (RC) analysis to evaluate defect formation, while cohesive energy density (CED) analysis assessed composite compatibility. These simulations guided experimental design (e.g., selecting functionalized GO and CNT via CED results), validated experimental observations through stress-strain curve comparisons, revealed reinforcement mechanisms (carbon nanomaterials regulate stress transfer, reduce defects, and promote PVA crystallization), and established a "simulation-guided, experiment-validated" research framework, providing theoretical tools and methodological references for interface engineering in polymer nanocomposites.

Abstract For studying the stress-strain state at singular points and their neighborhoods new concept is proposed. A singular point is identified with an elementary volume that has a characteristic size of the real body representative volume. This makes it possible to set and study the restrictions at that point. It is shown that problems with singular points turn out to be ambiguous, their formulation depends on the combination of the material and geometric parameters of the investigated body. Number of constraints in a singular point is redundant compared to the usual point of the boundary (it makes singular point unique, exclusive). This circumstance determines the non-classical problem formulation for bodies containing singular points. The formulation of a non-classical problem is given, the uniqueness of its solution is proved (under the condition of existence), the algorithm of the iterative-analytical decision method is described. Restrictions on the state parameters at the composite wedge vertex, one generatrix of which is in non-friction contact with a rigid surface are studied under temperature and strength loading. The proposed approach allows to identify critical combinations of material and geometric parameters that define the singularity of stress and strain fields close to singular representative volumes. The constraints on load components needed to solution existence are established. An example of a numerical analysis of the state parameters at the wedge vertex and its neighborhood is considered. Solutions built on the basis of a new concept, directly in a singular point, and its small neighborhood differ significantly from the solutions made with asymptotic methods. Beyond a small neighborhood of a singular point the solutions obtained on the basis of different concepts coincide.