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Phase Transformation, Functional Properties, and Crystallography of Advanced Materials (Second Volume)

A special issue of Materials (ISSN 1996-1944). This special issue belongs to the section "Materials Physics".

Deadline for manuscript submissions: 20 April 2025 | Viewed by 2312

Special Issue Editors

Prof. Dr. Zongbin Li

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Guest Editor
Key Laboratory for Anisotropy and Texture of Materials (Ministry of Education), School of Material Science and Engineering, Northeastern University, Shenyang 110819, China
Interests: shape memory alloys; martensitic transformation; crystallography; magnetocaloric effect; elastocaloric effect
Special Issues, Collections and Topics in MDPI journals
Dr. Jun Zhou

E-Mail Website
Guest Editor
Key Laboratory for Anisotropy and Texture of Materials (Ministry of Education), School of Materials Science and Engineering, Northeastern University, Shenyang 110819, China
Interests: nobel metal nanoparticles; nanocatalyst; structure catalyst

Special Issue Information

Dear Colleagues,

Solid-state phase transformation, as a classic topic in the field of materials science, has gained considerable attention for a long time. The use of such transformation not only allows substantial enhancement in the mechanical properties of structural materials but also induces some fascinating behaviors to functional materials. The discovery of some related functional activities in particular, e.g., shape memory effect, magnetocaloric effect and elastocaloric effect, has significantly promoted research progress. This Special Issue aims to provide a dedicated platform for sharing results concerning past accomplishments and future directions in the field of phase transformation, functional properties, and crystallography of advanced materials. We welcome review papers and original research articles on material design, microstructural characterization, and material property tuning, either via experimental techniques or theoretical approaches.

Prof. Dr. Zongbin Li
Dr. Jun Zhou
Guest Editors

Manuscript Submission Information

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Keywords

  • solid-state phase transformation
  • structural transformation
  • magnetic transition
  • microstructure
  • crystallography
  • shape memory alloys
  • magnetic shape memory alloys
  • magnetocaloric effect
  • elastocaloric effect
  • barocaloric effect

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Published Papers (3 papers)

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Research

14 pages, 9444 KiB  
Article
An Oriented Recrystallization Nucleation Mechanism of a Cold-Rolled Pure Ti with Electric-Pulse Treatment
by Qi Shi, Lei Wang, Xiu Song and Yang Liu
Materials 2024, 17(23), 5745; https://doi.org/10.3390/ma17235745 - 24 Nov 2024
Viewed by 414
Abstract
The effect of electric-pulse treatment (EPT) on the nucleation behavior of a cold-rolled pure Ti was investigated. The specimens are subjected to EPT and then annealed at 650 °C within 10 min. Both the electron backscatter diffraction (EBSD) and transmission electron microscope (TEM) [...] Read more.
The effect of electric-pulse treatment (EPT) on the nucleation behavior of a cold-rolled pure Ti was investigated. The specimens are subjected to EPT and then annealed at 650 °C within 10 min. Both the electron backscatter diffraction (EBSD) and transmission electron microscope (TEM) techniques were used for detailing the microstructural evolution of the specimens at the initial stage of recrystallization processing during annealing. The results show that oriented nucleation occurs in the EPTed specimen. The recrystallized grains form in a similar orientation with the deformed matrix grains, and the oriented nucleation originates from the deformed grains with <0001> poles tilted about 20° away from the normal direction (ND20 grains) in the EPTed specimen. Pyramidal <c + a> dislocations could be extensively activated in ND20 grains, while the activated dislocations were mainly on prismatic planes in the other oriented grains. Because the formation of sub-grains cannot be without the pyramidal <c + a> dislocation, oriented recrystallized grains easily form in the EPTed specimen. It is suggested that the increasing of pyramidal dislocation climbing activity is considered the key mechanism of the formation of sub-grains as well as oriented nucleation, resulting from high contents of vacancy induced by EPT. Full article
(This article belongs to the Special Issue Phase Transformation, Functional Properties, and Crystallography of Advanced Materials (Second Volume))
►▼ Show Figures

Figure 1

Figure 1
<p>EBSD IPF map of as-received pure Ti.</p> Full article ">Figure 2
<p>EBSD IPF maps and corresponding (0002) pole figures of (<b>a</b>,<b>c</b>) non-EPTed specimen; and (<b>b</b>,<b>d</b>) EPTed specimen.</p> Full article ">Figure 3
<p>EBSD IPF subset maps and corresponding (0002) pole figures only taken from recrystallized grains of (<b>a</b>,<b>c</b>) non-EPTed specimen; and (<b>b</b>,<b>d</b>) EPTed specimen after annealing.</p> Full article ">Figure 4
<p>IGMA distribution of (<b>a</b>) ND20 grains in non-EPTed specimen; (<b>b</b>) ND20 grains in EPTed specimen; (<b>c</b>) ND50–90 grains in non-EPTed specimen; and (<b>d</b>) ND50–90 grains in EPTed specimen.</p> Full article ">Figure 5
<p>TEM micrographs of EPTed specimen after annealing, showing (<b>a</b>) regular array of dislocations; (<b>b</b>–<b>d</b>) LAGBs; (e) dark field image of LAGB; and (<b>f</b>) sub-grains.</p> Full article ">Figure 6
<p>(<b>a</b>) EBSD IPF subset map of recrystallized grain (R) and deformed matrix grain (M); (<b>b</b>) corresponding (0002) pole figure of EPTed specimen after annealing.</p> Full article ">Figure 7
<p>TEM micrographs of EPTed specimen after annealing, showing sub-grains.</p> Full article ">Figure 8
<p>EBSD IPF maps and corresponding (0002) pole figures of recrystallized grains: (<b>a</b>,<b>c</b>) G1; and (<b>b</b>,<b>d</b>) G2.</p> Full article ">Figure 9
<p>TEM micrographs of EPTed specimen after annealing, showing the dislocations with the &lt;c&gt; component on the basal planes under <b>g</b> = [0001].</p> Full article ">Figure 10
<p>(<b>a</b>) Local magnificent band contrast (BC) map superimposed with grain boundary component of EPTed specimen after annealing, showing classification of LAGB; (<b>b</b>,<b>c</b>) IGMA distribution of different groups of LAGBs.</p> Full article ">Figure 11
<p>Schematic illustration showing nucleation behavior of ND20 grain in EPTed and non-EPTed specimens. (<b>a</b>) ND20 grain in non-EPTed specimen; (<b>b</b>) ND20 grain in EPTed specimen; (<b>c</b>) Nucleation of ND20 grain in non-EPTed specimen; (<b>d</b>) Nucleation of ND20 grain in EPTed specimen.</p> Full article ">
15 pages, 8933 KiB  
Article
Giant Elastocaloric Effect and Improved Cyclic Stability in a Directionally Solidified (Ni50Mn31Ti19)99B1 Alloy
by Honglin Wang, Yueping Wang, Guoyao Zhang, Zongbin Li, Jiajing Yang, Jinwei Li, Bo Yang, Haile Yan and Liang Zuo
Materials 2024, 17(19), 4756; https://doi.org/10.3390/ma17194756 - 27 Sep 2024
Viewed by 716
Abstract
Superelastic shape memory alloys with an integration of large elastocaloric response and good cyclability are crucially demanded for the advancement of solid-state elastocaloric cooling technology. In this study, we demonstrate a giant elastocaloric effect with improved cyclic stability in a <001>A textured [...] Read more.
Superelastic shape memory alloys with an integration of large elastocaloric response and good cyclability are crucially demanded for the advancement of solid-state elastocaloric cooling technology. In this study, we demonstrate a giant elastocaloric effect with improved cyclic stability in a <001>A textured polycrystalline (Ni50Mn31Ti19)99B1 alloy developed through directional solidification. It is shown that large adiabatic temperature variation (|ΔTad|) values more than 15 K are obtained across the temperature range from 283 K to 373 K. In particular, a giant ΔTad up to −27.2 K is achieved by unloading from a relatively low compressive stress of 412 MPa at 303 K. Moreover, persistent |ΔTad| values exceeding 8.5 K are sustained for over 12,000 cycles, exhibiting a very low attenuation behavior with a rate of 7.5 × 10−5 K per cycle. The enhanced elastocaloric properties observed in the present alloy are ascribed to the microstructure texturing as well as the introduction of a secondary phase due to boron alloying. Full article
(This article belongs to the Special Issue Phase Transformation, Functional Properties, and Crystallography of Advanced Materials (Second Volume))
►▼ Show Figures

Figure 1

Figure 1
<p>(<b>a</b>) DSC curves for the directionally solidified (Ni<sub>50</sub>Mn<sub>31</sub>Ti<sub>19</sub>)<sub>99</sub>B<sub>1</sub> alloy; (<b>b</b>) compressive stress–strain curve measured at 293 K.</p> Full article ">Figure 2
<p>(<b>a</b>) EBSD orientation micrograph (IPF contrast) covering the longitudinal section for the (Ni<sub>50</sub>Mn<sub>31</sub>Ti<sub>19</sub>)<sub>99</sub>B<sub>1</sub> alloy and the corresponding inverse pole figure related to the SD; (<b>b</b>) backscattered electron (BSE) image for the directionally solidified alloy; (<b>c</b>) BSE image corresponding to the squared region of (<b>b</b>); (<b>d</b>) TEM bright field image and the corresponding selected-area electron diffraction (SAED) for the boron-rich secondary phase along the [<math display="inline"><semantics> <mrow> <mover accent="true"> <mrow> <mn>1</mn> </mrow> <mo mathvariant="normal">-</mo> </mover> </mrow> </semantics></math>11] axis.</p> Full article ">Figure 3
<p>(<b>a</b>) Superelastic loop of the directionally solidified alloy measured under compression at 293 K; (<b>b</b>) typical Δ<span class="html-italic">T<sub>ad</sub></span> profile under a compressive strain of 8% by applying and removing the compressive loading of 510 MPa at 293 K; (<b>c</b>) correlation between Δ<span class="html-italic">T<sub>ad</sub></span> and compressive strain under various strain rates tested at 293 K; (<b>d</b>) correlation between Δ<span class="html-italic">T<sub>ad</sub></span> and strain rate under various compressive strains tested at 293 K.</p> Full article ">Figure 4
<p>(<b>a</b>) Influence of strain rate on the superelastic response at various compressive strains tested at 293 K, by applying the maximum compressive loading of 350 MPa, 394 MPa, 415 MPa, 417 MPa, 445 MPa, and 506 MPa for the compressive strains of 3%, 4%, 5%, 6%, 7%, and 8%, respectively; (<b>b</b>) correlation between energy dissipation Δ<span class="html-italic">W</span> and compressive strain under various strain rates.</p> Full article ">Figure 5
<p>Graphical representation of <span class="html-italic">COP<sub>mat</sub></span> as a function of Δ<span class="html-italic">T<sub>ad</sub></span>.</p> Full article ">Figure 6
<p>(<b>a</b>) Temperature-dependent superelasticity of the present alloy subjected to a strain rate of 2.8 × 10<sup>−4</sup> s<sup>−1</sup> by applying a maximum compressive strain of 8%. The inset displays the evolution of critical stress <span class="html-italic">σ<sub>cr</sub></span> as the variation of temperature. (<b>b</b>) Δ<span class="html-italic">S<sub>iso</sub></span> induced by compressive loading under various compressive strains. (<b>c</b>) Δ<span class="html-italic">T<sub>ad</sub></span> profiles upon unloading measured at various temperatures. (<b>d</b>) Comparison of the elastocaloric properties between the present alloy and several typical elastocaloric materials [<a href="#B3-materials-17-04756" class="html-bibr">3</a>,<a href="#B10-materials-17-04756" class="html-bibr">10</a>,<a href="#B11-materials-17-04756" class="html-bibr">11</a>,<a href="#B15-materials-17-04756" class="html-bibr">15</a>,<a href="#B16-materials-17-04756" class="html-bibr">16</a>,<a href="#B20-materials-17-04756" class="html-bibr">20</a>,<a href="#B31-materials-17-04756" class="html-bibr">31</a>,<a href="#B39-materials-17-04756" class="html-bibr">39</a>,<a href="#B40-materials-17-04756" class="html-bibr">40</a>,<a href="#B49-materials-17-04756" class="html-bibr">49</a>,<a href="#B50-materials-17-04756" class="html-bibr">50</a>,<a href="#B51-materials-17-04756" class="html-bibr">51</a>,<a href="#B52-materials-17-04756" class="html-bibr">52</a>,<a href="#B53-materials-17-04756" class="html-bibr">53</a>,<a href="#B54-materials-17-04756" class="html-bibr">54</a>,<a href="#B55-materials-17-04756" class="html-bibr">55</a>,<a href="#B56-materials-17-04756" class="html-bibr">56</a>].</p> Full article ">Figure 7
<p>(<b>a</b>) Selective stress–strain curves during cyclic tests; (<b>b</b>) Δ<span class="html-italic">T<sub>ad</sub></span> profiles induced by loading and unloading for some selected cycles.</p> Full article ">Figure 8
<p>Comparison on the DSC curves for the samples before and after 12,000 mechanical cycles.</p> Full article ">Figure 9
<p>(<b>a</b>) Morphology of the longitudinal section after 12,000 mechanical cycles; (<b>b</b>) local BSE image showing the appearance of residual martensite after mechanical cycling; (<b>c</b>) fractured surface morphology after 13,000 cycles of mechanical tests.</p> Full article ">
13 pages, 7695 KiB  
Article
Texture-Differentiated Grain Growth in Silicon Steel: Experiments and Modeling
by Songtao Chang, Yuhui Sha, Gengsheng Cao, Fang Zhang and Liang Zuo
Materials 2024, 17(12), 3037; https://doi.org/10.3390/ma17123037 - 20 Jun 2024
Viewed by 778
Abstract
Grain growth for various texture components in silicon steel was investigated via experiments and modeling. It was found that the clustered spatial arrangement of grains with specific orientations significantly altered the local environment for grain growth and consequently resulted in texture-differentiated grain size [...] Read more.
Grain growth for various texture components in silicon steel was investigated via experiments and modeling. It was found that the clustered spatial arrangement of grains with specific orientations significantly altered the local environment for grain growth and consequently resulted in texture-differentiated grain size distribution (GSD) evolution. A novel local-field model was proposed to describe grain growth driven by continuous changing orientation and size distribution of adjacent grains. The modelling results show that the texture-differentiated grain growth in microstructure with grain clusters can produce a GSD with increased proportion in small-sized range and large-sized range by more than two-times, accompanied with an evident change in area fractions of various texture components. The effect of clustered spatial arrangement on grain growth can be precisely predicted, which is valuable to design and control the texture-differentiated GSD as well as the global GSD. Full article
(This article belongs to the Special Issue Phase Transformation, Functional Properties, and Crystallography of Advanced Materials (Second Volume))
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Figure 1

Figure 1
<p>Orientation image maps and constant <span class="html-italic">φ</span><sub>2</sub> = 0° and 45° sections of ODFs in primarily recrystallized (<b>a</b>,<b>c</b>,<b>e</b>) and annealed (<b>b</b>,<b>d</b>,<b>f</b>) silicon steel sheets.</p> Full article ">Figure 2
<p>Grain boundary misorientation distributions for all grains and major texture components in primarily recrystallized (<b>a</b>) and annealed (<b>b</b>) silicon steel sheets.</p> Full article ">Figure 3
<p>Orientation image maps of identical region of Goss grain clusters and surrounding matrix grains in primarily recrystallized (<b>a</b>,<b>c</b>,<b>e</b>) and annealed (<b>b</b>,<b>d</b>,<b>f</b>) silicon steel sheets. The regions of Goss grain clusters in primarily recrystallized sheets (marked as A, B, and C) and the identical region in further annealed sheets are depicted with black dashed lines. G1 and G2 are two grains with Σ5 and Σ9 boundaries between Goss grains, respectively.</p> Full article ">Figure 4
<p>Area fraction, average grain size, and maximum grain size in primarily recrystallized and annealed silicon steel sheets.</p> Full article ">Figure 5
<p>Grain size distribution in primarily recrystallized and annealed silicon steel sheets.</p> Full article ">Figure 6
<p>Representation of local-field model: (<b>a</b>) planar section of three-dimensional microstructure in polycrystalline materials, (<b>b</b>) planar section of three-dimensional microstructure with spherical grains, and (<b>c</b>) grain network in a planar section.</p> Full article ">Figure 7
<p>Measured and calculated grain size distributions for major texture components after grain growth annealing in silicon steel sheets.</p> Full article ">Figure 8
<p>Schematic of initial microstructure (<b>a</b>) and grain size distribution (<b>b</b>) for the case of specially oriented grains clusteringly and randomly embedded in randomly oriented grains used in <a href="#sec4dot2-materials-17-03037" class="html-sec">Section 4.2</a>.</p> Full article ">Figure 9
<p>The evolution of average grain size (<b>a</b>), area fraction (<b>b</b>), and grain size distribution (<b>c</b>,<b>d</b>) for the case of grain clusters embedded in randomly oriented grains.</p> Full article ">Figure 10
<p>Schematic of initial microstructure (<b>a</b>) and grain size distribution (<b>b</b>) for the case of various spatial arrangements of grains and various grain boundary properties used in <a href="#sec4dot3-materials-17-03037" class="html-sec">Section 4.3</a>.</p> Full article ">Figure 11
<p>The evolution of average grain size (<b>a</b>), area fraction (<b>b</b>), and grain size distribution (<b>c</b>,<b>d</b>) in the case of various spatial arrangements of grains and various grain boundary properties.</p> Full article ">
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