• Applied Chemistry for Engineering
• /
• v.10 no.3
• /
• pp.400-406
• /
• 1999

In an effort to obtain high efficiency in gas fired absorption chillers, a new working fluid has been developed with thc addition of the component of $LiNO_3$, LiCl and LiI to the conventional solution of $LiBr-H_2O$. The solubility and vapor pressure of the 4 component working fluid developed in this work were measured and compared to the results of $LiBr-H_2O$ solution. It was observed that there exists an optimal mole ratio of the inorganic salts in terms of solubility. The mole ratio of LiBr, $LiNO_3$ and LiCl was found to be around 5:1:1~2 in the $LiBr-LiNO_3-LiCl-H_2O$ mixture, and in the case of $LiBr-LiO_3-Lil-H_2O$ and $LiBr-Lil-LiCl-H_2O$ mixtures, the mole ratio of LiBr, $LiNO_3$ and Lil/ LiBr, LiI and LiCl were found to be around 5:1:1 and 5:1:0.5~1 respectively. The vapor pressure of the 4 component working fluid of the optimal mole ratio was increascd with adding the component of $LiNO_3$, LiCl and LiI except for $LiBr-LiNO_3-LiCl-H_2O$ mixture. The absorption capacity of $LiBr-LiNO_3-LiCl-H_2O$ mixture was obtained higher than that of $LiBr-H_2O$ mixture.

• Proceedings of the Korean Vacuum Society Conference
• /
• 2011.02a
• /
• pp.183-183
• /
• 2011

리튬 이온 배터리의 cathode 및 electrolyte 재료로 사용되는 LiCoO2을 sputtering이나 pulsed laser deposition을 이용하여 박막으로 증착하기 위해서는 target이 필요하다. Target은 원료 분말을 가압 성형한 후 고온에서 소결하여 제조된다. LiCoO2 target 제조과정에서 고밀도를 얻기 힘들고 Li 성분의 증발이 일어난다. 또한 Li2O 분말은 흡습성이 매우 크다. 본 연구에서는 시간과 온도를 조절하여 최적화된 소결 과정을 통해 target의 밀도가 이론밀도와 근사한 값을 갖도록 하고, LiCoO2 또는 Co3O4 분말에 각각 흡습성이 낮은 Li2CO3 분말을 첨가하여 Li 성분을 조절하였다. Li과 Co의 조성비가 1:1-2:1인 고밀도의 LiCoO2 target을 제조하여 박막 증착 후 Li과 Co의 조성비가 1:1이 되도록 하였다.

• Proceedings of the Korean Institute of Electrical and Electronic Material Engineers Conference
• /
• 2005.07a
• /
• pp.318-319
• /
• 2005

본 연구에서는 $LiCoO_2/LiNi_{1/3}Mn_{1/3}Co_{1/3}O_2$ 혼합 정극활물질로 사용하여 전극을 제작하고 성능을 평가하였다. $LiCoO_2/LiNi_{1/3}Mn_{1/3}Co_{1/3}O_2$와 $LiCoO_2$의 혼합비에 따른 충방전 거동 및 임피던스 변화를 측정하였다. 각 조성에서의 초기용량은 160 ~ 170 mAh/g 정도였으며, $LiNi_{1/3}Mn_{1/3}Co_{1/3}O_2$의 첨가 비율이 증가함에 따라 비용량이 증가하였으나 고율에서의 방전용량은 낮았다.

• Korean Journal of Acupuncture
• /
• v.19 no.1
• /
• pp.15-23
• /
• 2002

This study was carried to identify the component of Large Intestine Meridian Muscle in human, dividing into outer, middle, and inner part. Brachium and antebrachium were opened widely to demonstrate muscles, nerve, blood vessels and the others, displaying the inner structure of Large Intestine Meridian Muscle. We obtained the results as follows; 1. Meridian Muscle is composed of the muscle, nerve and blood vessels. 2. In human anatomy, it is present the difference between a term of nerve or blood vessels which control the muscle of Meridian Muscle and those which pass near by Meridian Muscle. 3. The inner composition of meridian muscle in human arm is as follows. 1) Muscle; extensor digitorum tendon(LI-1), lumbrical tendon(LI-2), 1st dosal interosseous muscle(LI-3), 1st dosal interosseous muscle and adductor pollicis muscle(LI-4), extensor pollicis longus tendon and extensor pollicis brevis tendon(LI-5), adductor pollicis longus muscle and extensor carpi radialis brevis tendon(LI-6), extensor digitorum muscle and extensor carpi radialis brevis mucsle and abductor pollicis longus muscle(LI-7), extensor carpi radialis brevis muscle and pronator teres muscle(LI-8), extensor carpi radialis brevis muscle and supinator muscle(LI-9), extensor carpi radialis longus muscle and extensor carpi radialis brevis muscle and supinator muscle(LI-10), brachioradialis muscle(LI-11), triceps brachii muscle and brachioradialis muscle(LI-12), brachioradialis muscle and brachialis muscle(LI-13), deltoid muscle(LI-14, LI-15), trapezius muscle and supraspinous muscle(LI-16), platysma muscle and sternocleidomastoid muscle and scalenous muscle(LI-17, LI-18), orbicularis oris superior muscle(LI-19, LI-20) 2) Nerve; superficial branch of radial nerve and branch of median nerve(LI-1, LI-2, LI-3), superficial branch of radial nerve and branch of median nerve and branch of ulna nerve(LI-4), superficial branch of radial nerve(LI-5), branch of radial nerve(LI-6), posterior antebrachial cutaneous nerve and branch of radial nerve(LI-7), posterior antebrachial cutaneous nerve(LI-8), posterior antebrachial cutaneous nerve and radial nerve(LI-9, LI-12), lateral antebrachial cutaneous nerve and deep branch of radial nerve(LI-10), radial nerve(LI-11), lateral antebrachial cutaneous nerve and branch of radial nerve(LI-13), superior lateral cutaneous nerve and axillary nerve(LI-14), 1st thoracic nerve and suprascapular nerve and axillary nerve(LI-15), dosal rami of C4 and 1st thoracic nerve and suprascapular nerve(LI-16), transverse cervical nerve and supraclavicular nerve and phrenic nerve(LI-17), transverse cervical nerve and 2nd, 3rd cervical nerve and accessory nerve(LI-18), infraorbital nerve(LI-19), facial nerve and infraorbital nerve(LI-20). 3) Blood vessels; proper palmar digital artery(LI-1, LI-2), dorsal metacarpal artery and common palmar digital artery(LI-3), dorsal metacarpal artery and common palmar digital artery and branch of deep palmar aterial arch(LI-4), radial artery(LI-5), branch of posterior interosseous artery(LI-6, LI-7), radial recurrent artery(LI-11), cephalic vein and radial collateral artery(LI-13), cephalic vein and posterior circumflex humeral artery(LI-14), thoracoacromial artery and suprascapular artery and posterior circumflex humeral artery and anterior circumflex humeral artery(LI-15), transverse cervical artery and suprascapular artery(LI-16), transverse cervical artery(LI-17), SCM branch of external carotid artery(LI-18), facial artery(LI-19, LI-20)

• Proceedings of the Korean Institute of Electrical and Electronic Material Engineers Conference
• /
• 2000.04b
• /
• pp.117-120
• /
• 2000

The relation of crystal phase and charge/discharge capacity of $Li[Li_yMn_{2-y}]O_4$ were studied for different degrees of Li substitution (y). All cathode material showed spinel phase based on cubic phase in X-ray diffraction. Other peaks didn't show in spite of the increase of y value in $Li[Li_yMn_{2-y}]O_4$. Ununiform of $Li[Li_yMn_{2-y}]O_4$ which calcinated by (111) face and (222) face was more stable than that of pure $LiMn_2O_4$. In addition, At TG analysis, calcined $Li[Li_{0.1}Mn_{1.9}]O_4$ exhibited much mass loss at $800{\mu}m$. The cycle performance of the $Li(Li_yMn_{2-y}]O_4$ was improved by the substitution of $Li^{1+}$ for $Mn^{3+}$ in the octahedral sites. Specially, $Li[Li_{0.08}Mn_{1.92}]O_4$ and $Li[Li_{0.1}Mn_{1.9}]O_4$ cathode materials showed the charge and discharge capacity of about 125mAh/g at first cycle, and about 95mAh/g after 70th cycle. It is excellent than that of pure $LiMn_2O_4$, which 125mAh/g at first cycle, 65mAh/g at 70th.

• Transactions on Electrical and Electronic Materials
• /
• v.7 no.2
• /
• pp.76-80
• /
• 2006

Well-defined orthorhombic $LiMnO_2\;and\;LiCo_{0.1}Mn_{0.9}O_2$ were synthesized by a solid-state reaction and quenching process. X-ray diffraction (XRD) results revealed that the as-synthesized powders showed an orthorhombic phase of a space group with Pmnm. The $Li/LiMnO_2\;and\;Li/LiCo_{0.1}Mn_{0.9}O_2$ cells were constituted and cycled galvanostatically in the voltage range of 2.0-4.3 V vs. $Li/Li^+$ at a current density of $0.5\;mA\;cm^{-2}$ at room temperature and $50^{\circ}C$, respectively. The results demonstrated that the highest specific capacity of $Li/LiMnO_2$ cells at room temperature and $50^{\circ}C$ was 95 and $155\;mAh\;g^{-1}$, respectively. As for $Li/LiCo_{0.1}Mn_{0.9}O_2$ cells, the highest specific capacity at room temperature and $50^{\circ}C$ was 160 and $250\;mAh\;g^{-l}$, respectively. It could be seen that the performance of $Li/LiCo_{0.1}Mn_{0.9}O_2$ cells was better than that of $Li/LiMnO_2$ cells.

• Journal of the Korean Crystal Growth and Crystal Technology
• /
• v.8 no.4
• /
• pp.660-666
• /
• 1998

We discussed structure, energy state, characteristics of thermal stability, and electrochemical properties of Li-GFICs, Li-PCICs, and Li-AGICs during the intercalation process. According to X-ray diffraction patterns, we observed phase of stage 2 mainly from Li-GFICs, while stage 1 phase as well as stage 2 from Li-PCICs. For the structure of Li-AGICs, stage 1 phase was dominant, but it was not possible to obtain pure stage 1 compound probably due to structural characteristics of artificial graphite. We measured energy state of the compounds to stage stability, and revealed that Li-AGICs and Li-GFICs were in more stable state than Li-PCICs. Therefore, those two compounds could be excellent candidate for energy reserve material. From the study of thermal degradation, Li-GFICs showed strong exothermic reaction at around 300 and $400^{\circ}C$. In the study of thermal stability of Li-AGIC at various temperatures, we observed that lithium was not completely deintercalated and high stage was maintained even at high temperature. In the case of charge, discharge, and electrochemical studies, Li-GFICs showed the best results.

• Journal of the Korean Electrochemical Society
• /
• v.10 no.4
• /
• pp.239-244
• /
• 2007

In order to investigate the effect of fluorine ion in the $Li_{1-x}FeO_2Li_xMnO_2$ (Mn/(Mn + Fe) = 0.8) cathode material, it was synthesized $Li_{1-x}FeO_{2-y}F_y-Li_xMnO_2$ (Mn/(Mn + Fe) = 0.8, $0.05{\le}y{\le}0.15$) cathode materials at $350^{\circ}C$ for 10hrs using solid-state method. $Li_{1-x}FeO_{2-y}F_y-Li_xMnO_2$ (Mn/(Mn + Fe) = 0.8, $0.0{\le}y{\le}0.1$ was composed many large needle-like particles of about $1-1.5\;{\mu}m$ and small particles of about 50-100 nm, which were distributed among the larger particles. However, $Li_{1-x}FeO_{1.85}F_{0.15}-Li_xMnO_2$ material showed slightly different particle morphology. The particles of $Li_{1-x}FeO_{1.85}F_{0.15}-Li_xMnO_2$ were suddenly increased and started to be a spherical type of particle shape. $Li/Li_{1-x}FeO_{1.9}F_{0.1}-Li_xMnO_2$ cell showed a high initial discharge capacity of 163 mAh/g and a high cycle retention rate of 95% after 50 cycles. The initial discharge capacity of $Li/Li_{1-x}FeO_{2-y}F_y-Li_xMnO_2$ ($0.05{\le}y{\le}0.15$) cells increased according to the increase of F content. However, the cycleability of this cell was very rapidly decreased when the substituted fluorine content is over 0.1. We suggested that too large amount of F ion fail to substitute into the $Li_{1-x}FeO_2-Li_xMnO_2$ structure, which resulted in the severe decline of battery performance.

• 한국전기화학회:학술대회논문집
• /
• 2001.10a
• /
• pp.41-41
• /
• 2001

• Journal of the Korean Chemical Society
• /
• v.45 no.3
• /
• pp.251-255
• /
• 2001

The structure of the lithium zinc borate LiZnBO3 has been established by single-crystal X-ray diffraction methods. It crystallizes in the triclinic space group P1(Z=2), with unit-cell parameters - $a=5.0915(9)\AA$, $b=5.059(1)\AA$, $c=6.156(1)\AA$, $V=120.6(1)\AA3$ , $\alpha=65.81(1)^{\circ}$, $\beta=65.56(1)^{\circ}$ and $\gamma=59.77(1)^{\circ}$. The structure was determined from 704 unique reflections and refined to the final residuals R=0.039 and wR=0.056. It is characterized by an association of BO3 triangles and LiO4 and ZnO4 tetrahedra. The Li and Zn atoms are disordered around the average positions between Li1 and Li2 atoms or between Zn1 and Zn2 atoms. The disorder can be described by four half-occupied positions about Li1, Li2, Zn1 and Zn2 atoms.