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Article

Specimen Size Effect on the Tensile Properties of Rolled Steel of Long-Term-Operated Portal Crane

by
Olha Zvirko
1,*,
Ihor Dzioba
2,
Myroslava Hredil
1,
Robert Pała
2,
Oleksandr Oliynyk
3 and
Piotr Furmańczyk
2
1
Department of Diagnostics of Materials Corrosion-Hydrogen Degradation, Karpenko Physico-Mechanical Institute of the NAS of Ukraine, 5 Naukova St., 79060 Lviv, Ukraine
2
Department of Machine Design, Faculty of Mechatronics and Mechanical Engineering, Kielce University of Technology, Av. 1000-an. of Polish State, 7, 25-314 Kielce, Poland
3
Department of Lifting and Transport Machines and Engineering of Port Technological Equipment, Odessa National Maritime University, 34, Mechnikova St., 65029 Odesa, Ukraine
*
Author to whom correspondence should be addressed.
Materials 2023, 16(8), 3017; https://doi.org/10.3390/ma16083017
Submission received: 20 March 2023 / Revised: 3 April 2023 / Accepted: 6 April 2023 / Published: 11 April 2023
(This article belongs to the Special Issue Investigations and Modelling of the Fracture Process in Metallic Materials (Second Volume))
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Abstract

:
This paper presents the research results on the mechanical behavior of the low-carbon rolled steel of a sea portal crane after a 33-year operation depending on the operational stresses and rolling direction in order to assess its serviceability. The tensile properties of steels were investigated using rectangular cross-section specimens with different thicknesses and the same width. Strength indicators were slightly dependent on the considered factors (operational conditions, the cutting direction, and thickness of specimens). However, a clear trend of higher ultimate strength for thinner specimens was noticed, especially in the case of more brittle material due to its operational degradation. Plasticity of the tested steel specimens was more sensitive to the influence of the above-mentioned factors than strength but less sensitive than impact toughness. Uniform elongation was slightly less for thinner specimens regardless of the investigated steel state or the orientation of specimens relative to the rolling direction. The post-necking elongation was lower for transversal specimens compared with longitudinal ones, and the effect was more significant when testing steel with the lowest brittle fracture resistance. Among the tensile properties, non-uniform elongation was demonstrated to be the most effective for assessing the operational changes in the state of rolled steels.

1. Introduction

Stress-strain curves are widely used to determine tensile mechanical properties of materials, namely, strength and plasticity. Together with fracture toughness at quasi-static loading conditions or impact toughness, these characteristics are considered to be the basic mechanical properties of the material, and they are most often included in regulations for structural steels. The mechanical properties of steels are dependent not only on intrinsic microstructural features, such as the grain size and structure of the precipitated particles [1,2,3,4], but also on extrinsic testing conditions, such as strain rate [5,6], specimen geometry and size [4,7,8,9,10,11,12,13], and temperature [14,15,16]. Therefore, testing conditions and the geometry and dimensions of specimens are regulated by standards [17,18]. However, tensile specimens with different thicknesses and geometries are sometimes used [1,9], especially for testing materials with geometric size limitations, such as a metal sheet. Moreover, there is no exact requirement for the specimen thickness in standards.
Specimen-size effect on the tensile properties has been considerably studied recently for materials with different microstructures. In many cases, specimens with a rectangular cross section were used, and their size influenced the tensile properties of materials [1,7,9,19,20,21], including strength and plasticity. The influence of the gauge length on the tensile properties was studied in [7], showing that both total elongation and uniform elongation decrease with an increase in the gauge length/width ratio. At the same time, it was demonstrated that the intrinsic deformation is not dependent on the gauge length [7]. It was revealed in [9] that upper and lower yield strength, tensile strength, and post-necking elongation increase with increasing thickness of specimens with a rectangular cross section. Both uniform elongation and post-necking elongation increase with increasing specimen thickness, and such changes are mainly attributed to the necking behavior of the specimens [7].
Anisotropy of materials is a commonly observed phenomenon, especially for steels produced by rolling. Therefore, the mechanical properties of rolled steels vary depending on the direction along which they are measured [6,9,22,23,24,25,26,27,28]. The main causes of anisotropy are predominant crystallographic orientation (texture) and alignment and distribution of secondary phases, such as inclusions, in the microstructure. A commonly accepted experimental test used to characterize anisotropy of properties of textured rolled steels is the uniaxial tensile test using specimens cut out in different orientation relative to the rolling direction. Three main orientations are most often considered, namely, longitudinal (along the rolling of the plate), transverse (transverse to the rolling direction of the plate), and short transverse (perpendicular to the rolled plate surface). Nevertheless, the regulating documents and standards do not always specify the direction of specimen cutting relative to rolling, while longitudinal specimens are usually used because transversal or short transversal ones are sometimes impossible to cut out due to the size limitations of an object. One example of this is the case of testing thin-wall pipes with a small diameter made of rolled sheet steels [22].
In general, the resistance to fracture is the lowest for short transversal specimens and the highest for longitudinal ones [25,27]. It is usually the result of a weaker cohesion between the layers of texture and between the matrix and non-metallic inclusions elongated along the rolling direction, which promotes damage evolution in those sites [25,26,27,29]. In transversal specimens, the fracture propagates along the rolling direction, and it is facilitated due to existing areas with a reduced cohesive strength potentially susceptible to delamination or damages in the form of delaminations in the case of long-term-operated steel [26,27]. As a result, fracture mode is more brittle for transversal specimens compared with longitudinal ones [27,30].
In addition, operational degradation of structural steels [31,32,33,34,35,36,37,38,39,40] should also be taken into account. It is well-known that the long-term operation of steels often leads to a significant loss of the mechanical properties that ensure the serviceability of the material under certain loading conditions. The main peculiarity of in-service degradation consists primarily in the development of in-bulk damages at the nano- and micro-scale [26,41] that lead to a drop in plasticity and brittle fracture resistance and often cause abrupt failures. A crucial role of operational cyclic loading in in-bulk degradation of carbon steels of seaport hoisting and transporting equipment has been recently demonstrated in research [38,39]. Structures operated long-term under cyclic loading are subjected to strain hardening as well as fatigue crack initiation. Steel degradation manifests itself in a significant deterioration of impact toughness, and the higher the stress level, the lower the resistance to brittle fracture. For the rolled steels, cohesive strength between the matrix and non-metallic inclusions, elongated in the rolling direction, significantly reduces during operation [35,37]. It leads to enhancing the anisotropy of plasticity and the resistance to brittle fracture. The influence of long-term operation on the anisotropy of rolled steels is still under consideration. Moreover, studies [27,31] have shown that the anisotropic mechanical behavior of rolled pipeline steels is influenced by long-term operation. Recent studies [31,32,37,42] have demonstrated that transverse specimens were more suitable for the assessment of the degradation degree of steels. Therefore, an important research issue is the effect of damages in rolled steel due to operational degradation on the size factor manifestation based on the stress-strain curves.
The objective of this paper is to evaluate the mechanical behavior of portal crane rolled steel depending on operational stresses and rolling direction in order to assess its serviceability.

2. Materials and Testing Methods

The object of research is a portal crane (Figure 1) made of rolled sheet steel (low-carbon steel with ferrite-pearlite structure) after a 33-year operation in a seaport in Ukraine [39]. The averaged chemical composition of the steel was as follows: mass. %: 0.17 C; 0.23 Si; 0.54 Mn; 0.11 Cr; 0.01 S; 0.01 P; 0.10 Cu; and Fe—balance. The crane was manufactured from the same grade steel with the basic mechanical properties that met the specifications they were supplied to. The crane was subjected to approximately 5.3 × 106 cycles during operation.
The crane was operated under the action of cyclic loading and environmental impact. Operational factors which affect the serviceability of seaport hoisting and transporting equipment are considered in detail in [39]. Cyclic stresses are generally supposed to be the main factor in the operational degradation of portal crane metal [33,34,38,39]. Various crane units (Figure 1a) were subjected to mechanical cyclic loads of different intensities, which could contribute to operational degradation of the metal of certain structural elements due to strain hardening as a main mechanism of degradation. Combining the strain gauge method and calculations, cyclic stress ranges at the sheet surface Δσe have been evaluated for certain conditions of a loading-unloading cycle of the crane close to operational ones. First of all, the calculation of the stress-strain state of different sections of a portal crane was carried out using the finite element method in the ANSYS. After that, the most critical section zones and, accordingly, the sites for adjustment of the strain gauges on the portal crane were determined, and then strain measurements were carried out. Strains at different points of the crane (ten in total, indicated in Figure 1a) were measured using strain gauges under the loading-unloading cycle with an applied load close to the operational one. After that, cyclic stress ranges at the sheet surface were determined as the difference in stresses measured at the maximum cyclic load (crane under loading) and in unloading conditions. The applied technique is described in detail in [38]. It should be noted that the results of the numerical evaluation of stress distributions in crane units and field measurements practically coincided.
Considering previously evaluated impact toughness for the metal of the tested crane units [38], a general regularity has been found for all tested samples (Figure 2): the more cyclic stress range, the less impact toughness (e.g., brittle fracture resistance). It was supposed that the metal of the tested sections would not be identical in the initial state, and that their mechanical properties might slightly vary from piece to piece. In addition, the thickness of the plates also varied (10; 12; 16 and 25 mm). However, given the revealed regularity, it is suggested that operational conditions (cyclic stresses) are the crucial factor causing an enormously low-impact toughness of the most stressed components of the operated crane.
Based on the determined cyclic stress ranges, two crane sections with high and low cyclic stress ranges were chosen for further mechanical testing, as illustrated in Figure 1b. The first one is a lower shelf of the jib made of steel sheet with a thickness of 16 mm (steel A), and the second is a back shelf of the boom with a sheet thickness is 12 mm (steel B). The difference in Δσe values is significant for the tested crane sections: 55.0 MPa and 130.0 MPa for steels A and B, respectively (Table 1). Therefore, it can be suggested that the degradation degree of the studied steels is different. Although the degradation degree of steel from each section can’t be quantitatively evaluated because of a lack of information about its initial characteristics, the present research is believed to provide at least a qualitative comparison of the actual technical state of two crane units subjected to significantly different operational loads under long-term (33 years) operation.
The microstructures of the steels were observed using scanning electron microscopy (SEM). The studied steels had similar ferrite-pearlite microstructures, as shown in Figure 3. The microstructure of steel B (Figure 3b,d) was characterized by smaller average grain size compared to that of steel A (Figure 3a,c).
Test methods. We tested the steel from two crane sections, A and B (Figure 1), which differ significantly by the determined cyclic stress ranges (Table 1).
Since the degradation of metal manifests itself firstly in the drop of brittle fracture resistance due to the realization of a less energy-consuming fracture mechanism [33,35,37,38,39], impact toughness as a measure of the resistance to brittle fracture has been evaluated for the metal from both tested crane sections. Standard specimens 10 mm × 10 mm × 55 mm with a V-type notch for impact toughness testing were cut out from crane sections in longitudinal (L-T, direction of the global crack propagation was transverse) and transverse (T-L, the crack was propagated in longitudinal direction) directions relative to the plate processing geometry. Tests were performed according to ASTM E23-07a standard [43].
Basic mechanical properties were evaluated by tensile testing of flat specimens cut out longitudinally and transversely to the rolling direction of steel sheets. Two series of specimens with different gauge dimensions (thickness t × width × length) were used: 5.0 × 3.5 × 20.0 mm and 1.2 × 3.5 × 20.0 mm. Thickness is considered crucial in specimen distinctions; manufacturing flat specimens of a small thickness is easier than cylindrical ones. The research plan thus included eight types of specimens used for experiments (Table 2). Specimens were subjected to uniaxial tensile tests with the strain rate 3∙10−3 s−1 in air at ambient temperature according to ASTM E8 standard [17].
Besides standard mechanical properties under tension (yield stress σYS, ultimate stress σUTS and elongation ε), the parameter of relative elongation to failure ε (total elongation) was divided into two components, uniform relative elongation εu (before necking) and non-uniform one εn (during necking until fracture, that is, post-necking relative elongation), ε = εu + εn. Uniform elongation was determined as the elongation at the maximum load.
Experimental tensile tests were carried out using the Zwick-100 testing machine equipped with an automated control data recording system (Figure 4). Markings were made every 2.0 mm on the measuring section of the specimens. During the tensile test, the elongation on the measuring part was recorded using a video camera. The real-time recording of the elongation made it possible to determine the increment of the measuring section, the uniform elongation—εu and non-uniform one—εn. Additional markings on the measuring sections, together with the use of video recording, also made it possible to determine the actual strain in the material specimens at each stage of its loading [44].
Fractographic and metallographic testing has been performed using SEM–JEOL JSM-7100F.

3. Experimental Results and Discussion

3.1. Impact Toughness Testing

The impact strength values of the studied steels from two crane units showed a remarkable difference (Table 3). Thus, impact toughness of steel A was lower by approx. 50% for both longitudinal and transversal specimens compared to that of steel B.
The impact fracture surfaces of the longitudinal and transverse specimens of the studied steels are presented in Figure 5. The investigated specimens showed mostly ductile fracture. However, delaminations were also revealed for both steels, which were more pronounced for steel A, especially for the transverse specimen, compared with steel B (Figure 5c,d). This indicates that steel A operated under higher stresses (Table 1) and, characterized by lower resistance to brittle fracture (Table 3), is susceptible to low-energy delamination along the rolling direction (Figure 5c).
The results confirmed the suggestion about the crucial effect of operational cyclic stresses on the steel state. Indeed, the KCV level of steel A with higher cyclic stresses is twice as low in comparison with steel B (Table 1 and Table 3). In addition, the impact toughness of transverse specimens KCVT-L is approx. 2.5 times less than that of the longitudinal ones KCVL-T for both studied steels. This could be considered as an indicator of the operational degradation of steel since the ratio KCVT/KCVL for rolled steel is usually close to 0.7 and rarely drops to 0.5 [25,26,27]. Similar results have been obtained by other researchers [45] and explained by more pronounced delaminations along the texture layers in more degraded steel. However, the present study is not aimed at elucidating the mechanisms of the operational degradation of the tested pieces of metal; further research is focused on its consequences, trying to specify the plasticity parameters suitable for assessing the degree of operational degradation of portal crane steel.
Thus, the chosen material for the investigation reveals signs of operational degradation. It can be suggested that steel A is characterized by a higher degradation degree than steel B.

3.2. Stress–Strain Curves

Figure 6 depicts the experimentally measured stress-strain curves of the tested specimens. The average values of strength and plasticity characteristics determined by tensile testing of the investigated steels are presented in Table 4.
Ultimate strength divides the stress-strain curve into two parts: the former illustrates uniform elongation and the latter—non-uniform elongation under necking (post-necking elongation). In general, the changes in ultimate strength due to the considered factors (the operational stresses, the cutting direction of specimens and their thickness) are small, but some trends can be noted (Figure 7): ultimate strength characteristics are slightly higher for steel A compared with that determined for steel B. In our case, definitely higher σUTS values were obtained for thinner specimens, especially for more embrittled material A. With increasing thickness, both the strain-hardening part and the necking portion in the stress-strain curves of the studied steels are prolonged to a higher strain resulting in a larger overall ductility (Figure 6a,b).
As can be seen from Figure 7, steel B showed a pronounced strength anisotropy depending on the plane of fracture propagation relative to the rolling direction of the plate at testing specimens with different thickness. For material A, anisotropy in ultimate strength was only observed when testing the thinner specimens.
The main attention has been paid to the analysis of steel plasticity depending on its operational condition (comparison of materials A and B), texture (longitudinal and transversal specimens) and specimen thickness.

3.3. Elongation

Steel B, with a higher brittle fracture resistance KCV than steel A, expectedly has higher plasticity determined by total elongation ε. This regularity, in general, is valid regardless of the cutting direction of the specimens and their thickness (Figure 8a). Concerning the influence of specimen thickness on their plasticity, the total elongation of both steel states is significantly lower for thinner specimens regardless of their cutting direction due to a larger volume of the material in the gauge section in a thicker specimen, resulting in a higher elongation. Therefore, the specimen with higher thickness better resists crack growth and fracture during necking.
The discussed regularities of the influence of the operational conditions, specimen cutting direction and their thickness on steel plasticity are the results of the influence of these factors on its components εu and εn, which reflect the features of deformation and fracture of specimens at the stages of uniform elongation and necking. Significant changes in either component inevitably contribute to the parameter of total elongation ε.
Uniform elongation is sensitive to the considered factors with the same regularities as for total elongation ε: the value εu is noticeably lower for more embrittled steel A regardless of the specimen thickness (Figure 8b). Obviously, this component plays a key factor in the formation of total elongation ε. Concerning the effect of specimen thickness on the parameter εu, the regularity is the same as in the case of the total elongation ε: uniform elongation is somewhat lower for thinner specimens regardless of the steel state and specimen cutting. The obtained results are consistent with the research [7,21], demonstrating the effect of the size factor on the plasticity of the metal at the stage of uniform elongation: it increases with increasing specimen thickness.
The anisotropy of uniform elongation was insignificant for both studied steels regardless of the thickness of specimens (Figure 8b). The results indicate a stronger manifestation of the factors leading to the transition from uniform elongation to necking when testing specimens with a thickness of 1.2 mm. Since the beginning of the neck formation is identified by reaching the maximum stress on the stress-strain curve and associated with the development of micro defects in the specimen cross-section, then the role of these defects in the thin specimen is manifested at a lower deformation.
Analyzing the influence of specimen thickness on non-uniform elongation εn of specimens cut out from the tested sections of the crane in different orientations (Figure 8c) revealed that this parameter for both steels is significantly higher for thicker specimens regardless of their orientation relative to the rolling direction. This result is consistent with findings of the research [7] demonstrating an increase of both uniform and post-necking elongation with increasing specimen thickness. Due to a low aspect ratio width/thickness in the tested specimens, a diffuse necking mode could be expected [19,46,47].
The comparison of materials A and B (Figure 8c) indicates a high sensitivity of the parameter εn in the assessment of their operational changes in a metal state regardless of the thickness of the tested specimens. In addition, the effect of texture on the parameter εn is also clearer: for both tested materials, elongation under necking is lower in the case of transversal specimens; the effect is more significant in more embrittled steel. This means that the assessment of the operational changes in a metal state is the most expedient by the parameter of non-uniform elongation εn using transversal specimens. Such a conclusion is consistent with the estimation of operational degradation of steel by the resistance to brittle fracture (impact toughness and fracture toughness) [37,42].
The results summarized in Figure 8 made it possible to identify the following regularities. The plasticity characteristics of the steel are more sensitive to the operational changes in metal state, texture, and specimen thickness than its strength but less sensitive than impact toughness (the effect of specimen thickness was not considered when evaluating KCV) which varied from 60 J/cm2 to 310 J/cm2 (by more than 5 times) whereas the elongation parameters changed by an approx. 10–25%.

3.4. Fractographic Analysis of Tensile Failures

The regularities of plastic deformation of specimens have been analyzed taking into account their macro and micro fractographic features. Figure 9 illustrates typical macro fracture surfaces of tensile specimens of different thicknesses and cutting directions on the example of more embrittled steel A, providing a general view of the cup and cone fracture. The component “cup” (central part of the fracture surface) is characterized by delamination, which is more pronounced for the transversal specimens (Figure 9b,d). It indicates that delaminations formed either during operation or mechanical testing directly contribute to the formation of the fracture surface. Concerning the size of the component “cone” (on the sides), it is visually smaller for the transversal specimens.
Even a cursory analysis of the ratio between “cup” and “cone” component sizes revealed a crucial distinction for the specimens of different thicknesses (Figure 9). This is essential since “cup” is formed by tearing under triaxial stress conditions, whereas “cone” is by the shear mechanism under the plane stress state. It can be noted that the total size of “cone” is approx. 1/3 of the size of “cup” for thicker specimens (~1.2 mm), whereas, for thinner ones, this ratio reaches 1/2 (~0.6 mm). However, the question about what is crucial in the steel plasticity, the total size of “cone” or its relative value (concerning the “cup” size), should be further clarified.
Micro fractographic analysis has been performed for specimens of both steel states cut out longitudinally and transversely relative to the rolling direction. A typical fracture mechanism for all analyzed specimens is micro void coalescence (Figure 10). Deep small voids prevail on the fracture surface of the longitudinal specimen of steel B. They were formed by stretching with subsequent fracture of partitions between adjacent pores near carbides and inclusions (Figure 10b). In contrast, the fracture surface of more embrittled steel A contains mainly shallow and larger voids formed by the shear mechanism (Figure 10a). In addition, the amount of roundish fracture elements (delaminations), initiated from a chain of small non-metallic inclusions and formed by shear, is bigger for the steel A, and they are larger (30–40 μm in diameter). This facilitated the localization of deformation, resulting, thus, in less elongation for more embrittled steel A by approx. 8%.
The amount of delaminations along the chains of non-metallic inclusions is significantly bigger (Figure 10d) for the transversal specimen of steel B compared to the longitudinal one although the fracture of partitions between adjacent delaminations is ductile with the formation of equiaxed voids and clearly outlined tearing edges. Concerning the transversal specimen of more embrittled steel A, the role of shear in the fracture of partitions between delaminations is more pronounced (Figure 10c) despite the predominance of micro-void relief. As a result, the height difference in the fracture surface relief is lower, and tearing edges were formed at the transitions between adjacent areas of micro shear. Thus, the operational changes in the state of steel A are more pronounced on the fracture surface of the transversal specimen, and they manifest by enhancing the role of shear in the fracture. Since the shear is the final stage in the fracture process of flat tensile specimens, then its predominance on the fracture surface of the transversal specimen of steel A is in agreement with its lower plasticity compared to steel B by approx. 10%.

3.5. Future Research Prospects

Further research will be focused on the influence of the shape and dimensions of specimens loaded by uniaxial tension on the plasticity characteristics of the material under non-uniform strain. Experimental studies will be supplemented with numerical modelling to clarify the influence of the specimen shape on the evolution of stress and strain fields occurring during the neck formation. As a result, formulas will be obtained which describe the relationship between true stresses and strains, taking into account the specific dimensions of structural elements. The research will enable determining the limitations and proper solutions for the correct assessment of the operational changes in a metal state for the rolled structural steels when the structure is made of sheets of the same steel grade but with different thicknesses, taking into account the anisotropy of its mechanical properties.

4. Conclusions

Based on the investigations of long-term-operated sheet steel of a portal crane, the influence of certain factors, i.e., the operational conditions, specimen cutting direction and thickness, on strength and plasticity has been analyzed, distinguishing the components of uniform and non-uniform elongation. The performed analysis made it possible to formulate the following conclusions.
Strength indicators are not sensitive to the considered factors (the operational stresses, the cutting direction of specimens and their thickness). However, a clear trend of higher ultimate strength for thinner specimens is noticed, especially in the case of more brittle material.
Plasticity of the tested steel specimens, in general, is sensitive to the influence of the above-mentioned factors but less sensitive than impact toughness KCV. Uniform elongation is slightly lower for thinner specimens regardless of the state of the investigated steel and the orientation of specimens relative to the rolling direction. Among the plasticity parameters, non-uniform elongation is the most effective for assessing the operational changes in the steel regardless of thickness of specimens. In addition, post-necking elongation is lower in the case of transversal specimens, and the effect is more significant in more embrittled steel.
The results demonstrate that it would be advantageous to use the parameter of the non-uniform elongation εn determined using transversal specimens as the most sensitive for the assessment of the operational changes in a metal state for rolled sheet steels among the tensile properties.

Author Contributions

Conceptualization and methodology, O.Z., I.D. and M.H.; investigation, O.Z., I.D., M.H., R.P., O.O. and P.F.; writing—original draft preparation, O.Z., I.D. and M.H.; writing—review and editing, O.Z. and I.D. All authors have read and agreed to the published version of the manuscript.

Funding

The research was funded by Grant of the Ministry of Science and Higher Education of Poland No. 01.0.13.00/1.02.001/SUBB MKKM.23.002.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Data available on the request to the corresponding author.

Conflicts of Interest

The authors declare no conflict of interest.

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Materials 16 03017 g001 550
Figure 1. Schemes of a portal crane indicating the points for cyclic stress evaluation (a) and units chosen for present research (b): A–steel A, B–steel B.
Figure 1. Schemes of a portal crane indicating the points for cyclic stress evaluation (a) and units chosen for present research (b): A–steel A, B–steel B.
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Materials 16 03017 g002 550
Figure 2. Dependence between impact toughness KCV and cyclic stress range Δσe for steel cut out from various crane units. Units chosen for present research (A and B) are marked.
Figure 2. Dependence between impact toughness KCV and cyclic stress range Δσe for steel cut out from various crane units. Units chosen for present research (A and B) are marked.
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Materials 16 03017 g003 550
Figure 3. The SEM photographs of steel microstructure in longitudinal (a,b) and transverse directions (c,d): (a,c)—steel A; (b,d)—steel B.
Figure 3. The SEM photographs of steel microstructure in longitudinal (a,b) and transverse directions (c,d): (a,c)—steel A; (b,d)—steel B.
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Materials 16 03017 g004 550
Figure 4. Photographs of the tensile test specimens before test (a) and after test (b).
Figure 4. Photographs of the tensile test specimens before test (a) and after test (b).
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Materials 16 03017 g005 550
Figure 5. Fracture surfaces of the longitudinal L-T (a,b) and transverse T-L (c,d) specimens after impact toughness testing: (a,c)—steel A; (b,d)—steel B.
Figure 5. Fracture surfaces of the longitudinal L-T (a,b) and transverse T-L (c,d) specimens after impact toughness testing: (a,c)—steel A; (b,d)—steel B.
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Materials 16 03017 g006 550
Figure 6. Stress–strain curves of steel A (a) and B (b) for thinner (1, 2) and thicker (3, 4) specimens of transverse (1, 3) and longitudinal (2, 4) orientation.
Figure 6. Stress–strain curves of steel A (a) and B (b) for thinner (1, 2) and thicker (3, 4) specimens of transverse (1, 3) and longitudinal (2, 4) orientation.
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Materials 16 03017 g007 550
Figure 7. The average strength of steel A (1, 2) and B (3, 4) determined using specimens of transverse (1, 3) and longitudinal (2, 4) orientation.
Figure 7. The average strength of steel A (1, 2) and B (3, 4) determined using specimens of transverse (1, 3) and longitudinal (2, 4) orientation.
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Materials 16 03017 g008 550
Figure 8. The average total elongation (a), uniform elongation (b), and non-uniform elongation (c) of steel A (1, 2) and B (3, 4) determined using specimens of transverse (1, 3) and longitudinal (2, 4) orientation.
Figure 8. The average total elongation (a), uniform elongation (b), and non-uniform elongation (c) of steel A (1, 2) and B (3, 4) determined using specimens of transverse (1, 3) and longitudinal (2, 4) orientation.
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Materials 16 03017 g009 550
Figure 9. Examples of the macro fracture surfaces of specimens made from steel A with a thickness of 5.0 mm (a,b) and 1.2 mm (c,d), cut out along (a,c) and across (b,d) the rolling direction.
Figure 9. Examples of the macro fracture surfaces of specimens made from steel A with a thickness of 5.0 mm (a,b) and 1.2 mm (c,d), cut out along (a,c) and across (b,d) the rolling direction.
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Materials 16 03017 g010 550
Figure 10. Fracture surfaces of specimens with a thickness of 5.0 mm from steel A (a,c) and steel B (b,d), cut out along (a,b) and across (c,d) the rolling direction.
Figure 10. Fracture surfaces of specimens with a thickness of 5.0 mm from steel A (a,c) and steel B (b,d), cut out along (a,b) and across (c,d) the rolling direction.
Materials 16 03017 g010
Table
Table 1. Cyclic stress ranges at the surface of considered crane units.
Table 1. Cyclic stress ranges at the surface of considered crane units.
SteelCrane UnitSheet Thickness [mm]Cyclic Stress Range Δσe [MPa]
AJib16.0130.0
BBoom12.055.0
Table
Table 2. Specimen marking depending on their cutting orientation and thickness.
Table 2. Specimen marking depending on their cutting orientation and thickness.
SteelSpecimen
Orientation		Specimen Code for
t1 = 5.0 mm		Specimen Code for
t2 = 1.2 mm
ALongitudinalA-L-t1A-L-t2
TransverseA-T-t1A-T-t2
BLongitudinalB-L-t1B-L-t2
TransverseB-T-t2B-T-t2
Table
Table 3. Impact toughness experimentally observed for studied steels.
Table 3. Impact toughness experimentally observed for studied steels.
SteelCrane UnitKCVL-T [J/cm2] 1KCVT-L [J/cm2] 2
AJib15960
BBoom310123
1 KCVL-T—impact toughness determined using longitudinal specimens. 2 KCVT-L—impact toughness determined using transverse specimens.
Table
Table 4. Mechanical properties of the tested specimens evaluated by tensile testing.
Table 4. Mechanical properties of the tested specimens evaluated by tensile testing.
Specimen CodeσYS
[MPa]		σUTS
[MPa]		ε
[mm/mm]		εu
[mm/mm]		εn
[mm/mm]
A-L-t12824370.3190.1800.139
A-T-t12834390.3050.1740.131
B-L-t12984300.3470.1920.155
B-T-t13004340.3400.1890.151
A-L-t22974790.2750.1720.103
A-T-t23004660.2650.1680.097
B-L-t23054480.3030.1850.118
B-T-t23224680.2970.1830.114
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MDPI and ACS Style

Zvirko, O.; Dzioba, I.; Hredil, M.; Pała, R.; Oliynyk, O.; Furmańczyk, P. Specimen Size Effect on the Tensile Properties of Rolled Steel of Long-Term-Operated Portal Crane. Materials 2023, 16, 3017. https://doi.org/10.3390/ma16083017

AMA Style

Zvirko O, Dzioba I, Hredil M, Pała R, Oliynyk O, Furmańczyk P. Specimen Size Effect on the Tensile Properties of Rolled Steel of Long-Term-Operated Portal Crane. Materials. 2023; 16(8):3017. https://doi.org/10.3390/ma16083017

Chicago/Turabian Style

Zvirko, Olha, Ihor Dzioba, Myroslava Hredil, Robert Pała, Oleksandr Oliynyk, and Piotr Furmańczyk. 2023. "Specimen Size Effect on the Tensile Properties of Rolled Steel of Long-Term-Operated Portal Crane" Materials 16, no. 8: 3017. https://doi.org/10.3390/ma16083017

APA Style

Zvirko, O., Dzioba, I., Hredil, M., Pała, R., Oliynyk, O., & Furmańczyk, P. (2023). Specimen Size Effect on the Tensile Properties of Rolled Steel of Long-Term-Operated Portal Crane. Materials, 16(8), 3017. https://doi.org/10.3390/ma16083017

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