The influence of scan strategy on the residual stress (RS) state of an as‐built IN718 alloy produced by means of laser powder bed fusion (LPBF) is investigated. Two scan vector rotations (90°‐alternation and 67°‐rotation), each produced following two different scan vector lengths (long and short), are used to manufacture four rectangular prisms. Neutron diffraction (ND) and laboratory X‐ray diffraction (XRD) techniques are used to map the bulk and surface RS state, respectively. The distortion induced upon removal from the baseplate is measured via profilometry. XRD measurements show that the two long scan vector strategies lead to higher RS when compared with the equivalent short scan vector strategies. Also, the 67°‐rotation strategies generate lower RS than their 90°‐alternation counterparts. Due to the lack of reliable stress‐free references, the ND results are analyzed using von Mises stress. In general, ND results show significant RS spatial non‐uniformity. A comparison between ND and distortion results indicates that the RS component parallel to the building direction (Z‐axis) has a predominant role in the Z‐displacement. The use of a stress balance scheme allows to discuss the variability along the length of the specimens, as well as examine the absolute RS state.

Rapid cooling rates and steep temperature gradients are characteristic of additively manufactured parts and important factors for the residual stress formation. This study examined the influence of heat accumulation on the distribution of residual stress in two prisms produced by Laser Powder Bed Fusion (LPBF) of austenitic stainless steel 316L. The layers of the prisms were exposed using two different border fill scan strategies: one scanned from the centre to the perimeter and the other from the perimeter to the centre. The goal was to reveal the effect of different heat inputs on samples featuring the same solidification shrinkage. Residual stress was characterised in one plane perpendicular to the building direction at the mid height using Neutron and Lab X-ray diffraction. Thermography data obtained during the build process were analysed in order to correlate the cooling rates and apparent surface temperatures with the residual stress results. Optical microscopy and micro computed tomography were used to correlate defect populations with the residual stress distribution. The two scanning strategies led to residual stress distributions that were typical for additively manufactured components: compressive stresses in the bulk and tensile stresses at the surface. However, due to the different heat accumulation, the maximum residual stress levels differed. We concluded that solidification shrinkage plays a major role in determining the shape of the residual stress distribution, while the temperature gradient mechanism appears to determine the magnitude of peak residual stresses.

The magnetic structures of ${}^{153}{\mathrm{EuMn}}_2{\mathrm{Ge}}_2$ and ${}^{153}{\mathrm{EuMn}}_2{\mathrm{Si}}_2$ have been determined by neutron diffraction measurements (∼1.8–723 K). The Mn sublattices of both ${\mathrm{EuMn}}_2{\mathrm{Ge}}_2$ and ${\mathrm{EuMn}}_2{\mathrm{Si}}_2$ order antiferromagnetically $[T_N=667\mathrm{}(9)\mathrm{}\mathrm{K};$ space group ${I4\mathrm{}}^{\prime }{/m}^{\prime }{m}^{\prime }m$ and $T_N=391\mathrm{}\left(5\right)\mathrm{}\mathrm{K};$ space group $I_p{4/m}^{\prime }{m}^{\prime }{m}^{\prime },$ respectively] with no evidence for ordering of the ${\mathrm{Eu}}^{+2\mathrm{}}$ ions in ${\mathrm{EuMn}}_2{\mathrm{Ge}}_2$ down to 1.5 K. ${\mathrm{EuMn}}_2{\mathrm{Si}}_2$ exhibits a thermally driven valence transition around $T_v\sim 527\mathrm{K}$ with a pronounced increase in the unit cell volume of ∼7% from the ${\mathrm{Eu}}^{3+}$ state at low temperatures $(T<\mathrm{}\sim 150\mathrm{K})$ to an average valence state of ∼2.5 at high temperatures $(T>\mathrm{}\sim 600\mathrm{K}).\mathrm{}$ The valence-induced volume changes have been analyzed for the first time in terms of the interconfigurational fluctuation model with occupation probabilities for the ${\mathrm{Eu}}^{2+}$ state in ${\mathrm{EuMn}}_2{\mathrm{Si}}_2$ and the average ${\mathrm{Eu}}^{\mathrm{val}}$ values found to agree well with our reanalysis of earlier ${}^{151}{\mathrm{EuMn}}_2{\mathrm{Si}}_2$ isomer shift data. The strength of the magnetic interaction for antiferromagnetic ordering of the Mn sublattice is decreased by ∼10%–15% as a result of the change in the electronic configuration of