• 한국재료학회지
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• 제5권3호
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• pp.364-370
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• 1995

ex-AUC U$O_{2}$ 분말과 $Gd_{2}$O_{3}$ 분말을 기계적으로 혼합하여 소결한 U$O_{2}$-$Gd_{2}$O_{3}$ 소결체의 밀도 변화와 재소결 후 밀도변화를 기공크기 및 분포의 변화로 서술하였다. 수소분위기에서 175$0^{\circ}C$, 4시간 동안 소결하였을 때, 순수 U$O_{2}$의 소결밀도는 97.2% T.D.였으나 6wt% $Gd_{2}$O_{3}$ 첨가까지는 U$O_{2}$-$Gd_{2}$O_{3}$의 소결밀도는 $U^{+4}$와 $Gd^{+4}$의 상호확산 때문에 약 90% T.D.로 급격히 감소하였다. 그러나 6wt% 이상의 $Gd_{2}$O_{3}$가 첨가되면 우라늄이온 산화아와 산소침입으로 인하여 소결밀도는 오히려 증가하였다. 1$700^{\circ}C$에서 재소결시킬 때 순수 U$O_{2}$ 소결체에서는 재소결 시간에 따라 밀도증가가 발생하였다. U$O_{2}$-$Gd_{2}$O_{3}$ 소결체 경우에는 재소결시 밀도가 감소하였으나 재소결 시간이 증가함에 따라 다시 밀도는 증가하였고, 6wt%$Gd_{2}$O_{3}$가 첨가된 U$O_{2}$-$Gd_{2}$O_{3}$ 소결체에서 밀도가 가장 많이 감소하였다.

• 한국세라믹학회지
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• 제40권9호
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• pp.916-920
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• 2003

무게 비로 6%의 Gd가 치환된 이산화 우라늄, ( $U_{0.913}$G $d_{0.087}$) $O_2$를 475$^{\circ}C$ 공기 분위기에서 산화시키고 130$0^{\circ}C$ 공기 분위기에서 열처리시킬 때 변화하는 결정 구조, 형상 등을 XRD, SEM 및 EPMA 등을 이용하여 관찰하였다. 입방계 구조의 ( $U_{0.913}$G $d_{0.087}$) $O_2$는 475$^{\circ}C$ 공기 분위기에서 사방정게 구조의 ( $U_{0.913}$G $d_{0.087}$)$_3$ $O_{8}$로 산화되었다. 저온 산화에 의해 생성된 사방정계 130$0^{\circ}C$의 고온에서 열처리하는 동안 사방정계 상과 압방정계 상으로 다시 분리되었다. XRD와 EPMA 관찰결과, 분리된 사방정계 상과 입방정계 상은 각각 $U_3$ $O_{8}$과 ( $U_{0.67}$G $d_{0.33}$) $O_{2+}$x/인 것을 확인하였다. 열처리 동안 일어나는 일련의 산화와 상 분리 과정은 상 반응식으로 나타낼 수 있다. 각 열처리 단계에서의 무게 변화비를 측정하고 상 반응식을 이용하면 (U,Gd) $O_2$에 고용되어 있는 초기 Gd 함량을 정확히 계산할 수 있다.

• 한국전기전자재료학회:학술대회논문집
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• 한국전기전자재료학회 1999년도 추계학술대회 논문집
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• pp.594-597
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• 1999

The new green and red phosphors for PDP application activated by T $b^{3+}$ and E $u^{3+}$ were synthesized, and their photoluminance properties were investigated. It was found that the brightness of $Al_3$Gd $B_4$ $O_{12}$ :T $b^{3+}$ green phosphor under 147nm VUV irradiation was higher than that of commercial Z $n_2$ $SiO_4$:M $n^{2+}$ phosphor. But the emitting intensity of A1$_3$Gd $B_4$ $O^{12}$ :E $u^{3+}$ red phosphor was inferior to the commercial (Y,Gd)B $O_3$:E $u^{3+}$. $Al_3$Gd $B_4$ $O_{12}$ Phosphor had a strong excitation band at 160nm associated with the host absorption, and also the photoluminance excitation intensity of $Al_3$Gd $B_4$ $O_{12}$ :T $b^{3+}$ was higher than that of Z $n_2$ $SiO_4$:M $n^{2+}$, but the intensity of $Al_3$Gd $B_4$ $O_{12}$ :E $u^{3+}$ phosphor was smaller than (Y,Gd)B $O_3$:E $u^{3+}$ phosphor In the VUV range. C $e^{3+}$ co-doping in A1$_3$Gd $B_4$ $O^{12}$ :E $u^{3+}$ and substitution of $Al^{3+}$ by G $a^{3+}$ A1$_3$Gd $B_4$ $O^{12}$ :E $u^{3+}$ phosphor were tried, but they did not improved the optical property .d the optical property .ty .

• Nuclear Engineering and Technology
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• 제52권6호
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• pp.1099-1109
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• 2020

The performance of gadolinium burnable absorber (GdBA) for reactivity control in UO₂ and (U, Th)O₂ fuels and its impact on spent fuel characteristics was performed. Five fuel assemblies: one without GdBA fuel rod and four each containing 16, 24, 34 and 44 GdBA fuel rods in both fuels were investigated. Reactivity swing in all the FAs with GdBA rods in UO₂ fuel was higher than their counterparts with similar GdBA fuel rods in (U, Th)O₂ fuel. The excess reactivity in all FAs with (U, Th)O₂ fuel was higher than UO₂ fuel. At the end of single discharge burn-up (~ 49.64 GWd/tHM), the excess reactivity of (U, Th) O₂ fuel remained positive (16,000 pcm) while UO₂ fuel shows a negative value (-6,000 pcm), which suggest a longer discharge burn-up in (U, Th)O₂ fuel. The concentration of plutonium isotopes and minor actinides were significantly higher in UO₂ fuel than in (U, Th)O₂ fuel except for ²³⁶Np. However, the concentration of non-actinides (gadolinium and iodine isotopes) except for ¹³⁵Xe were respectively smaller in (U, Th)O₂ fuel than in UO₂ fuel but may be two times higher in (U, Th)O₂ fuel due to its potential longer discharge burn-up.

• Nuclear Engineering and Technology
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• 제33권3호
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• pp.307-314
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• 2001

The changes of weight gain, structure, morphology and uranium oxidation states in l0wt% G $d_2$ $O_3$-doped U $O_2$ during the oxidation below 475$^{\circ}C$ and heat treatment at 130$0^{\circ}C$ in air were investigated using TGA, XRD, SEM, EPMA and XPS. The room temperature ( $U_{0.86}$G $d_{0.14}$) $O_2$Cubic Phase Converted to highly distorted ( $U_{0.86}$G $d_{0.14}$)$_3$ $O_{8}$ -type sing1e Phase by oxidation at 475 $^{\circ}C$ in air. This oxidized phase was reduced by annealing at 130$0^{\circ}C$ in air. The room temperature XRD pattern of the 130$0^{\circ}C$ annealed powder revealed that ( $U_{0.86}$G $d_{0.14}$)$_3$ $O_{8}$ -type single phase was separated into Gd-depleted $U_3$ $O_{8}$ and Gd-enriched ( $U_{0.7}$G $d_{0.3}$) $O_2$$_{+x}$ type cubic phase. The reduction and phase separation by the high temperature annealing of kinetically metastable and highly deformed ( $U_{0.86}$G $d_{0.14}$)$_3$ $O_{8}$ -type phase are interpreted in terms of cation size difference between G $d^3$$^{+}$ and U according to the oxidation state of U.U.U.U.U.te of U.U.U.U.U.

• 한국원자력학회:학술대회논문집
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• 한국원자력학회 2002년도 춘계공동학술발표회요약집
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• pp.417.2-417
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• 2002

• 한국분말야금학회:학술대회논문집
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• 한국분말야금학회 2005년도 춘계학술강연 및 발표대회강연 및 발표논문 초록집
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• pp.50-51
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• 2005

• 한국세라믹학회:학술대회논문집
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• 한국세라믹학회 2003년도 춘계총회 및 연구발표회 초록집
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• pp.90.1-90
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• 2003

• Nuclear Engineering and Technology
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• 제36권1호
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• pp.104-111
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• 2004

The melting temperatures of $UO_2,\;UO_2-6wt\%Gd_{2}O_3,\;UO_2-12wt\%Gd_{2}O_3,\;UO_2-2wt\%Er_{2}O_3,\;and\;UO_2-4wt\%Er_{2}O_3$ fuels were measured. Fuel materials were loaded in a tungsten capsule of which shape met the black body condition. The melting temperature was measured by the thermal arrest method during heating of the capsule in an induction furnace. The measured melting temperature of $UO_2$ fuel was $2815{\pm}20^{\circ}C$. The solidus and liquidus temperatures of $UO_2-Gd_{2}O_3\;and\;UO_2-Er_{2}O_3$ had also been measured, and it was observed that the solidus temperatures of them were lower than the liquidus temperature by $15{\sim}25^{\circ}C$. Measured melting temperatures of $UO_2,\;UO_2-Gd_{2}O_3\;and\;UO_2-Er_{2}O_3$ fuels were as follows:

• 한국원자력학회:학술대회논문집
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• 한국원자력학회 2001년도 춘계학술발표회요약집
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• pp.271.1-271
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• 2001