• Journal of the Korean Ceramic Society
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• v.33 no.7
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• pp.832-838
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• 1996

Thermite reaction products of MgO and Al were added to MgO-C refractory to improve the properties of corrosion against the attack of slag, oxidation and mechanical spalling. Corrosion rate of MgO-C-MgAl2O4 spinel refractory at the ratio of 3.3(CaO/SiO2) slag was smaller than that of MgO-C and MgO-C-Al refractory. The excellent corrosion resistance of the MgO-C-MgAl2O4 spinel refractory against the slag attack was appeared by Al and MgAl2O4 spinel with high melting point and corrosion resistance and the high thermal conductivity and low thermal expansion of AIN. Hot M.O.R at 140$0^{\circ}C$ and the resistance of oxidation weight loss at 90$0^{\circ}C$ were 210kg/cm2 and -12% respectively.

• Journal of the Korean Ceramic Society
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• v.35 no.2
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• pp.129-136
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• 1998

The effects of MgO on the resistance to corrosion and oxidation of Al2O3-SiC-C refractory have been in-vestigated. The resistance to oxidation was improved as the amount of MgO increased. The resistance to corrosion was enhanced until 2 wt% MgO content but degraded over that content. From the dependence of temperatuer on the oxidation resistance oxidation was suppressed by the microstructural densification caused by spinel formation over 1200~130$0^{\circ}C$and the formation MgO-Al2O3-SiO2 liguid-phase over 130$0^{\circ}C$ The weight loss of specimens containing MgO with various purity at range of 95 to 99% and par-ticle size of -0.045 mm to -0.074 mm was examined. The oxidation resistance was not changed signficantly with the particle size and purity of MgO powders.

• Resources Recycling
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• v.18 no.3
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• pp.49-54
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• 2009

The effect of MgO in synthesis of alinite clinker was investigated. Clinker of alinite composition ratio and alintite clinker substituted for MgO of 3.77% were sintered at $760^{\circ}C$ and between $800^{\circ}C$ and $1,400^{\circ}C$ at the interval of $100^{\circ}C$. Synthesized phases and hydration heat of alinite clinker with MgO and without MgO were then investigated. As a result, alinite, CCA, ${\beta}-C_2S$ and f-CaO phases are synthesized in alinite clinker without MgO sintered at $1,300^{\circ}C$, while only alinite phase is synthesized in alinite clinker with MgO sintered at $1,300^{\circ}C$ with the highest synthesis rate. Heat evolution of alinite clinker with MgO has no induction period.

• Journal of the Korean Ceramic Society
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• v.25 no.6
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• pp.593-600
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• 1988

The properties of 10 kinds of MgO clinker were investigated to know the effect of MgO clinker's porperties on corrosion of MgO-C brick. For MgO clinker, chemical composition, porosity, density, periclase grain size, and microstructure were examined, while slag corrosion resistance was examined for MgO-C brick. In MgO clinker pore size and it's distribution, periclase grain size, impurities composition and the composition of grain boundaries are more important factors to determine corrosion degree of MgO-C brick than density, potosity and MgO purity.

• Journal of the Korean Ceramic Society
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• v.23 no.1
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• pp.51-59
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• 1986

It was the first time the MgO-C brick was developed for the lining materials in the hot spots in electric are furnace in 1972. MgO-C brick is high registant to thermal and structural spalling. Futhermore for the reason that carbon is hard to react with slag and MgO is high fireproof MgO-C brick shows a high corrosion registance to slag attack compared with conventional basic refractories. Owing to their excellent properties the use of MgO-C refractories are being developed widely in the field of shaped refractories and even in that of monolithic refractories. In this paper the oxidation of carbon the infiltration of slag into the brick texture and effects of additions were investigated. The results obtained were as follows : 1) The use of fused MgO-clinker and high purity carbon as raw materials increased the corosion registance and hot modulus of rupture of MgO-C brick. 2) As the oxidation reaction of the carbon proceeded the slag infiltrated into the brick texture. And then the slag components reacted with the MgO grains and formed low melting point compounds particulary CaO.MgO.$SiO_2$ and 3CaO.MgO.$2SiO_2$ that resulted in the wear of the brick. 3) It is recongnized the Al, Si, $B_3C$ effects on the oxidation registant properties of MgO-C brick by contribu-ting to the decrease of permeability according to the formation of $Al_4C_3$, SiC, $B_2O_3$ and the decrease of open pores relating to the formation of MgO.Al2O3, $SiO_2$, 3MgO.$B_2O_3$ at the decarbonized layer.

• Proceedings of the Korean Vacuum Society Conference
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• 2000.02a
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• pp.68-68
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• 2000

펄스레이저 증착법(이하 PLD)을 이용하여 마이크로파 유전체 소자 및 절연 산화막으로의 응용을 위한 MgTiO3 박막을 다양한 기판상에서 증착하였다. 사파이어 기판에 (a,c-plane Al2O3) 성장된 MgTiO3 박막은 에피텍셜 성장(epitaxial growth)이 되었으며, SiO2/Si 및 Pt/Ti/Si 기판위세 성장된 MgTiO3 박막의 경우 003방향으로 배향(oriented) 되었다. MgTiO3 박막은 450~75$0^{\circ}C$까지 기판온도를 변화시키면서 증착시켰으며, 증착시 산소분압은 50~200 mTorr로 변화시켰다. PLD 증착시 타켓에 조사된 레이저 에너지 밀도는 약 2J/cm2였으며, MgTiO3 박막 증착후 200Torr O2 분위기에서 상온까지 1$0^{\circ}C$/min 의 속도로 냉각시켰다. 사파이어 c-plane 상에서 일머나잇(ilminite) MgTiO3 구조가 55$0^{\circ}C$ 에피텍셜 성장하는 것을 관찰할 수 있었으며, 사파이어 a-plane 상에서는 MgTiO3 구조가 $650^{\circ}C$ 이상부터 110방향으로 배향되며 성장하였다. $600^{\circ}C$ 이상에서 c-축으로 배향된 구조를 갖고 있었다. 증착된 MgTiO3 박막의 조성분석(stoichio metric analysis)을 위해 RBS 분석을 수행하여, 증착에 이용된 타켓과 동일한 조성을 갖는 MgTiO3 박막이 성장된 것을 확인할 수 있었다. 사파이어 기판상에 증착된 MgTiO3 박막은 가시영역에서 투명하였으며, 약 270nm 파장을 갖는 영역에서 급격한 흡수단을 보였다. 이때의 MgTiO3 박막은 AFM 분석을 통해 약 0.87mn rms roughness 값을 갖는 매우 평탄한 표면구조를 갖고 있는 것을 확인하였다. MIM(Pt/MgTiO3/Pt) 구조의 캐패시터를 형성시켜 MgTiO3 박막의 유전특성(dielectric properties)을 관찰하였다. PLD로 성장된 MgTiO3 박막의 유전율(relative dielectric constant)은 약 22였으며, 1MHz에서 약 1.5%의 유전손실(dielectirc loss) 값을 보였다. 또한 이때 MgTiO3 박막은 낮은 유전분산값을 보였다.

• Journal of the Korean Ceramic Society
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• v.27 no.2
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• pp.233-243
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• 1990

For theinvestigation of MgO addition effect on 12Ce-TZP ceramics, MgO-CeO2-ZrO2 ceramics was fabricated using commercial powders under sintering condition of 130$0^{\circ}C$-1$600^{\circ}C$ for 2hr. Fully tetragonal phase could be obtained by proper heat treatment and MgO addition amount. Minor cubic phase was appeared in relatively high MgO content composition at each sintering temperature. As alloying amount of MgO increased, tetragonal stability increased and grain size decreased. Grain size dependence on MgO content was verified by SEM observation of fractured surface. Surface bloating was observed from the 2 m/o to 6m/o in the temperature range of 150$0^{\circ}C$ to 1$600^{\circ}C$. In spite of very porous microstructure owing to surface bloating, 100% TZP could be maintained in 2.0m/o MgO composition by heat treatment of 150$0^{\circ}C$. This result indicated that MgO was more powerful stabilizer than CeO2. Mechanical proprties of MgO-CeO2-ZrO2 ceramics were consistent with the stability observation of tetragonal phase very well.

• Journal of the Korean Ceramic Society
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• v.40 no.6
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• pp.530-538
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• 2003

Samples with the nominal composition, B $i_{1.84}$P $b_{0.34}$S $r_{1.91}$C $a_{2.03}$C $u_{3.06}$ $O_{10+}$$\delta$/ (110 K phase) high $T_{C}$ superconductors containing MgO as an additive were fabricated by a solid-state reaction method. Samples with 5~50 wt％ MgO were sintered at 820~86$0^{\circ}C$ for 24 h. The structural characteristics, critical temperature and grain size of the samples with different MgO contents were analyzed by XRD and SEM. As the MgO content increased, the intensity of MgO peaks and ratio of Bi-2212 phase in superconductors were intensified and the proportion of the phase transition from Bi-2223 to Bi-2212 was increased.d.creased.d.

• Journal of the Korea Academia-Industrial cooperation Society
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• v.14 no.9
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• pp.4185-4190
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• 2013

We executed the property changes of the sintered MgO (99.9% purity, 300nm size) specimens with addition to CaO content of 0.00wt%, 0.25wt%, and 0.50wt%, processed at 7GPa, for 5min, 600~$800^{\circ}C$. To investigate the micro-structure and physical property changes of the sintered MgO(-CaO), we employed a scanning electron microscopy(SEM), X-ray diffractomerty(XRD), Vickers hardness, and density. The SEM result showed that MgO powder of 300nm size was changed into sintered structure of 520nm by high pressure and low temperature sintering, regardless of the CaO contents. According to the XRD analysis, no CaO phase observed, while MgO peaks shift indicated the existence of CaO in the MgO matrix. The Vickers hardness result showed that hardness of sintered MgO-CaO increased by 12% compared pure MgO under the same temperature conditions. It implied that we can obtain the same hardness with $100^{\circ}C$ lowered sintering temperatures by addition of CaO. The density results showed that it was possible to obtain density of 98%, which is 5% greater than that of pure MgO at low temperature of $600^{\circ}C$.

• Proceedings of the KIEE Conference
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• 2006.07c
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• pp.1420-1421
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• 2006

In this study, structural and micowave dielectric properties of the $Mg_{5}B_{4}O_{15}$ (B=Ta, Nb) cation-deficient perovskite ceeramics. The specimens are prepared through the solid-state route. According to the XRD pattern, $Mg_{4}Ta_{2}O_9$ and $MgTa_{2}O_6$ phase exist in calcined and sintered $Mg_{5}Ta_{4}O_{15}$ powder. Also $Mg_{5}Ta_{4}O_{15}$ phase added with increasing sintering temperature. In the case of calcined and sintered $Mg_{5}Nb_{4}O_{15}$ powder, single phase of $Mg_{5}Nb_{4}O_{15}$ were appeared. The bulk density and quality factor of the $Mg_{5}B_{4}O_{15}$ (B=Ta, Nb) ceramics were increased with sinteming temperature in $1400^{\circ}C{\sim}1450^{\circ}C$, but these were decreased in another sintering temperature. Dielectric constant of the $Mg_{5}Ta_{4}O_{15}$ ceramics was increased continuously with increasing of sintering temperature. And the dielectric constant of the $Mg_{5}Nb_{4}O_{15}$ ceramics was increased in $1400^{\circ}C{\sim}1450^{\circ}C$ but decreased in $1475^{\circ}C$. In the case of the $Mg_{5}Ta_{4}O_{15}$ and $Mg_{5}Nb_{4}O_{15}$ ceramics sintered at $1450^{\circ}C$ for 5h, the dielectric constant, quality factor, and temperature coefficient of the resonant frequency (TCRF) were 8.2, 259,473 GHz, -10.91 $ppm/^{\circ}C$ and 14, 37,350 GHz, -52.3 $ppm/^{\circ}C$, respectively.