• 한국자기학회:학술대회 개요집
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• 한국자기학회 2016년도 임시총회 및 하계학술연구발표회
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• pp.80-80
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• 2016

• 한국자기학회:학술대회 개요집
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• 한국자기학회 2016년도 자성 및 자성재료 국제학술대회
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• pp.60-61
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• 2016

• 한국분말야금학회:학술대회논문집
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• 한국분말야금학회 2000년도 추계학술대회 및 발표대회 강연 및 발표논문 초록집
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• pp.31-32
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• 2000

• 한국재료학회지
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• 제5권1호
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• pp.22-35
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• 1995

본 연구는 Mn-Al 합금계에서 $\tau$상의 분율이 가장 높은 기준 조성을 결정하고 이 기준 조성중 Mn 원자의 일부를 Cu와 Fe 원자로 치환하였을 때 $\tau$상의 안정성과 자기적 성질의 변화를 조사하엿다. Mn-Al 합금계에서 $\tau$상의 분률과 자기적 특성이 가장 높은 조성은 $Mn_{0.56}Al_{0.44}$이었다. $Mn_{0.56-X}M_{X}Al_{0.44}$ 합금계의 결정구조는 M=Cu의 경우, 노냉시편과 소둔시편은 x $\leq$ 0.08 범위에서 $\tau$상과 $\beta$-Mn상이 나타났고, 0.10 $\leq x \leq$ 0.12 범위에서는 $\tau$상과 $\kappa$상이 나타났으며, 0.15 $\leq$ 0.20 범위에서는 $\kappa$상만이 존재하였다. 급속응고시편은 x=0.04에서 $\varepsilon$상과 $\tau$상이 공존하였고, x=0.06 및 x=0.08에서는 $\kappa$상과 $\tau$상이 공존하였으며 x=0.12와 x=0.20에서는 $\kappa$ 상만이 존재하였다. M=Fe의 경우, 노냉시편은 x < 0.08 범위에서 $\tau$상, $\beta$-Mn상 및 $\gamma_{2}$상이 나타났고, x > 0.10 범위에서는 $\kappa$상과 $\beta$-Mn$상이 나타났다. 급속응고시편은 x $\leq$ 범위에서는 $\varepsilon$상과 $\gamma_{2}$상이 나타났지만, 미량의 $\tau$상과 $\kappa$상도 존재함을 알 수 있었다. X=0.12와 x=0.20에서는 $\kappa$상만이 존재하엿다. $Mn_{0.56}Al_{0.44}$ 합금에서 노냉시편과 소둔시편의 포화자화값은 40-45(emu/g)이었으며 curie 온도는 약 650K였다. 급속응고 시편의 포화자화값은 약 50-52(emu/g), Curie 온도는 약 644K엿다. 소둔시편 및 급냉리본 모두 큰 잔류자화/포화자화 비(~0.7)를 나타냈으며, 특히 급냉리본의 경우 77K에서 큰 잔류자화값(~48emu/g)을 보여주었다. $Mn_{0.56-X}M_{X}Al_{0.44}$ 합금계의 자기장에 따른 자화값의 변화는 강자성이 형태를 보여주었고 자화값은 강자성과 $\tau$상과 $\kappa$상의 분율에 따라 결정되며 M=Cu일때, 최대자발자화값은 x=0.15에서 약 64.5(emu/g)이었다. M=Fe일 때 자화값은 x=0.15에서 최대자발자화값($\sigma_{0.0}$=66.4emu/g)이 나타났으며 $\tau$상 영역에서의 값보다 높았다. Curie 온도는 M=Cu, Fe에 관계없이 x가 증가함에 따라 감소하였다.

• 분석과학
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• 제8권2호
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• pp.195-203
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• 1995

Fe-5.7% Al 합금에 탄소 및 미량 합금원소를 첨가하고 그 제진특성 변화를 결정립 크기 및 자기적 특성과 관련하여 관찰하였으며, 탄소의 거동을 XRD 및 EDS로 조사하였다. 이 합금은 강자성형 제진 양상을 나타냈고, 제3원소 첨가는 그 SDC를 악화시키며 특히 탄소는 현저하였다. 제진 특성은 결정립 크기와는 직접적인 상관관계가 없었고, 자기이력곡선 면적은 상관관계가 있었다. 탄소가 이 합금의 제진특성을 악화시키는 원인은 고용탄소에 의한 $90^{\circ}$ 자구벽의 고착이 주원인이었으며, 탄화물도 자구벽의 이동을 방해할 것이므로 제진특성에 악영향을 미치는 것으로 해석되었다.

• 한국자기학회지
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• 제5권5호
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• pp.515-518
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• 1995

We have studied the magnetization in fields up to 1T at 5K, the saturation magnetization dependence on temperature and the temperature dependence of AC-susceptibility at very low fields (5mOe to 50mOe) of glassy $Fe_{91-x}Zr_{7}B_{2}Ni_{x}$ (x = 0, 5, 10, 15) alloys. The temperature dependence of the magnetization follows the predictions of spin wave excitations with long wavelengths. At zero Ni concentration there is a clear competition between ferromagnetic and antiferromagnetic interactions giving rise to spin-glass behaviour. The addition of Ni drastically modifies the magnetic properties: the antiferromagnetic exchange coupling is reduced and finally disappears, the spin wave stiffness increases from 39.5 to $87.3\;meV{\AA}^{2}$ and To increases from 230 K to 478 K. We develop a simple model to quantify the competing interactions and to relate the antiferromagnetically coupled Fe moments to the Ni concentration. We find that the initial susceptibility increases with increasing Ni content along with a decrease of the temperature dependence.

• Journal of Magnetics
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• 제21권2호
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• pp.164-167
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• 2016

The effect of the B additions on glass formation and magnetic properties is reported for the $Fe_{(87-x-y)}Co_yTi_7Zr_6B_x$ (x = 2, 4, 6 and y = 35, 40) alloy system. The ribbon samples with the width of 2 mm for each composition were prepared by the melt spinning technique; furthermore, their phase information was obtained from X-ray diffraction. Glass formation and magnetic properties were measured using differential scanning calorimetry and vibrating sample magnetometer respectively. The $Fe_{45}Co_{40}Ti_7Zr_6B_2$ (x = 2 and y = 40) system has the nanocrystalline phase identified as ${\alpha}-Fe$, as well as the amorphous phase, whereas all other alloys are fully amorphous. It is associated with the role of B on the glass formation. The widest supercooled liquid region is obtained as 71 K at x = 4 (both y = 35 and 40). The saturation magnetization decreases with the increase of the amount of the B addition, and the highest value is 1.59 T as x = 2 and y = 35 for this alloy system.

• 대한전기학회:학술대회논문집
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• 대한전기학회 1996년도 하계학술대회 논문집 C
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• pp.1407-1408
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• 1996

The development of MCFC is going to the second stage of development and recent studies have been focusing on long-term durability of cell component. Systematic investigation on corrosion behavior of Fe-based alloys has been done in (62+38) mol % (Li+K) $CO_3$ melt at 923K by using steady-state polarization and electrochemical impedance spectroscopy method. It was found that the corrosion current t of these Fe-based alloys decreased with increasing Cr, Al content.

• Metals and materials international
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• 제24권6호
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• pp.1309-1314
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• 2018

In this study, we investigated the state of $Y_2O_3$, as a major additive element in Fe-based ODS alloys, during mechanical alloying (MA) processes by thermodynamic approaches and experimental verification. For this purpose, we introduced $Ti_2O_3$ that formed different reaction products depending on the state of $Y_2O_3$ into the Fe-based ODS alloys. In addition, the reaction products of $Ti_2O_3$, Y, and $Y_2O_3$ powders were predicted approximately based on their formation enthalpy. The experimental results relating to the formation of Y-based complex oxides revealed that $YTiO_3$ and $Y_2Ti_2O_7$ were formed when $Ti_2O_3$ reacted with Y; in contrast, only $Y_2Ti_2O_7$ was detected during the reaction between $Ti_2O_3$ and $Y_2O_3$. In the alloy of $Fe-Cr-Y_2O_3$ with $Ti_2O_3$, $YTiO_3$ (formed by the reaction of $Ti_2O_3$ with Y) was detected after the MA and heat treatment processes were complete, even though $Y_2O_3$ was present in the system. Using these results, it was proved that $Y_2O_3$ decomposed into monoatomic Y and O during the MA process.

• Bulletin of the Korean Chemical Society
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• 제2권3호
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• pp.96-104
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• 1981

(1) The flow data of f (stress) and ${\dot{s}$ (strain rate) for Fe and Ti alloys were plotted in the form of f vs. -ln ${\dot{s}$ by using the literature values. (2) The plot showed two distinct patterns A and B; Pattern A is a straight line with a negative slope, and Pattern B is a curve of concave upward. (3) According to Kim and Ree's generalized theory of plastic deformation, pattern A & B belong to Case 1 and 2, respectively; in Case 1, only one kind of flow units acts in the deformation, and in Case 2, two kinds flow units act, and stress is expressed by $f={X_1f_1}+{X_2f_2}$where $f_1\;and\;f_2$ are the stresses acting on the flow units of kind 1 and 2, respectively, and $X_1,\;X_2$ are the fractions of the surface area occupied by the two kinds of flow units; $f_j=(1/{\alpha}_j) sinh^{-1}\;{\beta}_j{{\dot{s}}\;(j=1\;or\;2)$, where $1/{\alpha}_j\;and\;{\beta}_j$ are proportional to the shear modulus and relaxation time, respectively. (4) We found that grain-boundary flow units only act in the deformation of Fe and Ti alloys whereas dislocation flow units do not show any appreciable contribution. (5) The deformations of Fe and Ti alloys belong generally to pattern A (Case 1) and B (Case 2), respectively. (6) By applying the equations, f=$(1/{\alpha}_{g1}) sinh^-1({\beta}_{g1}{\dot{s}}$) and $f=(X_{g1}/{\alpha}_{g1})sinh^{-1}({\beta}_{g1}{\dot{s}})+ (X_{g2}/{\alpha}_{g2})\;shih^{-1}({\beta}_{g2}{\dot{s}})$ to the flow data of Fe and Ti alloys, the parametric values of $x_{gj}/{\alpha}_{gj}\;and\;{\beta}_{gs}(j=1\;or\;2)$ were determined, here the subscript g signifies a grain-boundary flow unit. (7) From the values of ($({\beta}_gj)^{-1}$) at different temperatures, the activation enthalpy ${\Delta}H_{gj}^{\neq}$ of deformation due to flow unit gj was determined, ($({\beta}_gj)^{-1}$) being proportional to , the jumping frequency (the rate constant) of flow unit gj. The ${\Delta}H_{gj}\;^{\neq}$ agreed very well with ${\Delta}H_{gj}\;^{\neq}$ (self-diff) of the element j whose diffusion in the sample is a critical step for the deformation as proposed by Kim-Ree's theory (Refer to Tables 3 and 4). (8) The fact, ${\Delta}H_{gj}\;^{\neq}={\Delta}H_{j}\;^{\neq}$ (self-diff), justifies the Kim-Ree theory and their method for determining activation enthalpies for deformation. (9) A linear relation between ${\beta}^{-1}$ and carbon content [C] in hot-rolled steel was observed, i.e., In ${\beta}^{-1}$ = -50.2 [C] - 40.3. This equation explains very well the experimental facts observed with regard to the deformation of hot-rolled steel..