By performing solution treatment at various temperatures, creep property measurements, and microstructural observations, the influence of the solution temperature on the microstructure uniformity and high-temperature creep properties of the DZ125 nickel-based alloy were studied. The results showed that after the solution and aging treatment of the alloy under a relatively low temperature of 1230°C, microstructure inhomogeneities in the dendrite/inter-dendrite regions appeared, and the coarse g¢ phase and eutectic structure in the casted alloy were not removed. The processing and aging treatment of the alloy under a higher solution temperature of 1260°C caused the coarse g¢ phase and eutectic structure within the inter-dendritic area of the alloy to be eliminated, thus enabling the uniform distribution of the fine cubic g¢ phase with a high-volume fraction between the dendrite/inter-dendrite regions and the enhancement of the creep performance of the alloy.

The deformation characteristics of a single-crystal nickel-based alloy containing Re during creep at room temperature were studied by means of creep property tests, microstructure observations and contrast analysis of the dislocation configuration. The results show that during the deformation of the alloy at room temperature, the original cubic γ′ phase transforms into a rhombus shape along the direction of maximum shearing stress, and its deformation feature is that the dislocation slips in the matrix and shears the γ′ phase. The superdislocation shear into the γ′ phase can cross slip from the {111} plane to the {100} plane, forming a K-W lock, and can also be decomposed at the {111} plane. The dislocation configurations of (1/2) partial dislocation plus antiphase boundary (APB) and (1/3) partial dislocation plus SISF can effectively inhibit the slip and cross-slip of the dislocation and improve the deformation resistance of the alloy. At the later stage of creep, under the action of shear stress, the initial slip system is activated first to distort the γ and γ′ phases, and then the secondary slip system is activated and shears the primary slip system, resulting in a large stress concentration at the delivery point and the initiation of cracks in this area. With the alternating activation of the primary slip system and secondary slip system during creep, the initiation and expansion of cracks continue. Damage and fracture mechanisms occur in alloys during room temperature creep.

Magnetorheological elastomers (MREs) are field-responsive composites whose stiffness can be tuned by a magnetic field. In chain-like MREs, strong local magnetic interactions and Maxwell tractions do not necessarily translate into a measurable macroscopic response, because interfacial tractions may be internally balanced after elastic propagation. This study develops a Green-function-weighted traction-transfer framework describing how generalized misalignment modulates magnetoelastic transduction. Local interfacial magnetic traction is projected onto a prescribed macroscopic observable through an output-specific elastic influence field, and a transfer-efficiency index quantifies the contribution that survives weighted cancellation. A minimal two-source model and a dimensionless illustration show that misalignment can produce an output through magnetic-traction imbalance, elastic-transfer imbalance, or their combination, whereas compensating imbalances suppress it. A three-dimensional strong-field finite-element study (flux density up to 0.58 T, constant relative permeability µ _r = 200) resolves two effects in aligned and longitudinally offset chains under tension, compression, and shear: a strongly mode-dependent magneto-induced effect, reaching +36.0% in shear while tension is weak (+6.4%) and the compressive nominal stress is reduced, and an output-specific geometric effect in which, at matched strain, field, and particle volume fraction, the offset chain is stiffer in shear and compression while the two configurations are essentially equal in tension. The solver is verified against an analytic single-sphere solution (0.13% error) and a zero-field hyperelastic degeneracy test (0.0003% error). The transfer-efficiency index is evaluated directly from the finite-element fields and cross-validated against the macroscopic reaction force, giving near-unity transfer in the field-aligned channel and near-complete cancellation in the cross-mode channel. The framework yields a design guideline rather than a universal rule: enhancement occurs only when misalignment increases the product of available weighted traction and transfer efficiency for the selected output.

A high-performance TiAl-Nb alloy was obtained by forging and heat treatment. The tensile properties of the alloy were tested, and the microstructure of the alloy was observed via transmission electron microscopy (TEM) and scanning electron microscopy (SEM) with electron backscatter diffraction (EBSD). The results revealed that after the alloy undergoes tensile fracture at the temperature of 820 °C, the yield strength was 420 Mpa and the elongation rate is 3.6 %. After tensile fracture at 880 °C, the yield strength of the alloy was 340 Mpa and the elongation rate is 9.8 %.The brittle-ductile transition temperature (BDTT) of the alloy ranged from 820 °C to 880 °C. In the brittle fracture process, the alloy fractures by a mixed mode of lamellar fracture and lamellar colony boundary fracture. In lamellar colonies, cracks propagate mainly along the γ / γ interface. Among the lamellar colony boundaries, the passivated serrated lamellar colony boundary has better crack propagation resistance than the straight strip lamellar colony boundary. In the process of plastic fracture, lamellar colony boundary fracture is the main damage mechanism. The repeated recrystallization of γ grains and abundant B2 phase that precipitates within and between lamellar colonies are the main reasons for the formation and propagation of cracks.

The evolution of superdislocation structures during the creep of a single-crystal alloy was investigated through creep performance testing, microstructural observations, and comparative analysis of dislocation configurations. The results revealed that, in the early stage of creep, dislocations activated in the γ phase first glide along the {111} plane and subsequently reach the {100} γ / γ ′ interface. At this interface, they transform into 〈110〉 60° mixed dislocations, which gradually develop into a 〈110〉 dislocation network. As creep deformation proceeds, these 〈110〉 60° mixed dislocations progressively convert into 〈100〉 type dislocations at the γ / γ ′ {100} interface via a specific climb mechanism driven by mismatch stress, eventually forming a 〈100〉 dislocation network. During the middle and late stages of creep, dislocations begin to shear the rafted γ ′ phase sequentially, first single dislocations, then anti-phase boundary (APB) plus dislocation pairs, and finally superlattice intrinsic stacking faults (SISFs) plus partial dislocation. Consequently, the strain-softening mechanism during creep is governed not only by the increased density of specific superdislocations but also by the continuous evolution and interaction of multiple dislocation types.