Analisis Biaya Jaminan Kesehatan Masyarakat Dan Asuransi Kesehatan Pada Pasien Stroke Non-hemoragik Di Rumah Sakit Umum Daerah Kabupaten Sleman

Background: Non-hemorrhagic stroke causes many deaths.Its treatment requires long-term care, resulting in very highcost. Controlinging costs and quality are very important in maintainingsustainability, however, in reality there are cost sharingby patients and hospitals outside the insurance coverage.Aim: This study aims to identify the difference in cost thatmust be shared to the patient and the hospital for inpatientnon-hemorrhagic stroke of the Jamkesmas and Askes patientsin Sleman Hospital.Method: This study used a cross ssectional design. Datawere retrieved retrospectively with a primary diagnosis ofnon-hemorrhagic stroke hospitalizations for patients admittedto the hospital during the period of January 2011 to May 2012.Data were analyzed using univariate, bivariate correlation,and multivariate.Result: The average cost of inpatient care non-hemorrhagicstroke Jamkesmas patients was Rp3.541.021,00 +Rp2.609.488,00 and for Askes patients Rp4.678.509,00 +3.257.816,00. The average cost sharing in Askes patients isRp.1.851.536,00 + 1.968.757,00 and Jamkesmas isRp405.976,00 +Rp2.303.903,00. Percentage the greatest costcomponent in Askes patients is drugs (47%) and accomodation(44%), while in Jamkesmas is drug (52%) and accommodation(36%). Components of the cost sharing in Askes patients wasdrug (87%). The difference in the cost of hospital rates wasgreater than INA-CBGs respectively Rp3.541.021,00 +Rp2.609.488,00 and Rp3.135.045,00 + Rp727.710,00.Conclusion: The proportion of costs covered by the insuranceand shared by patient/hospital is 87:13 for Jamkesmaspatient, 55:45 for Askes patients (January 2011-May 2011),and 59:41 for the Askes patients (June 2011-May 2012). Theproportion of cost sharing of inpatient care non-hemorrhagicstroke by Askes patients outside the program is greater thanthe proportion of costs sharing by the hospital on Jamkesmasprogram

Mechanical and electrochemical properties of multiple-layer diode laser cladding of 316L stainless steel

In the present investigation, a detailed mechanical and electrochemical properties of multiple-layer laser clad 316L stainless steel (from the powders produced by gas atomized route) has been carried out. Multiple-layer laser cladding of 316L stainless steel has been conducted using a diode laser. The mechanical property (rmcrohardness) of the fabricated product has been evaluated using a microhardness testing machine and correlated with the process parameters. The electrochemical property, mainly pitting corrosion resistance of the fabricated layer corresponding to maximum microhardness (in a 3.56% NaCl solution) has been evaluated using standard potentiodynamic polarization testing. The microhardness of the laser assisted fabricated layers was found to vary from 170 to 278 VHN, increased with decrease in applied power density and increase in scan speed and was higher than that of conventionally processed 316L (155 VHN). The superior microhardness value is attributed to grain refinement associated with laser melting and rapid solidification. The critical potential to pit formation (E-PP1) was measured to be 550 mV saturated calomel electrode (SCE) and superior to the conventionally processed 316L stainless steel (445 mV (SCE)). (c) 2005 Elsevier B.V. All rights reserved

Laser processing of materials

Light amplification by stimulated emission of radiation (laser) is a coherent and monochromatic beam of electromagnetic radiation that can propagate in a straight line with negligible divergence and occur in a wide range of wave-length, energy/power and beam-modes/configurations. As a result, lasers find wide applications in the mundane to the most sophisticated devices, in commercial to purely scientific purposes, and in life-saving as well as life-threatening causes. In the present contribution, we provide an overview of the application of lasers for material processing. The processes covered are broadly divided into four major categories; namely, laser-assisted forming, joining, machining and surface engineering. Apart from briefly introducing the fundamentals of these operations, we present an updated review of the relevant literature to highlight the recent advances and open questions. We begin our discussion with the general applications of lasers, fundamentals of laser-matter interaction and classification of laser material processing. A major part of the discussion focuses on laser surface engineering that has attracted a good deal of attention from the scientific community for its technological significance and scientific challenges. In this regard, a special mention is made about laser surface vitrification or amorphization that remains a very attractive but unaccomplished proposition

Laser Surface Engineering of Metallic Components

The engineering solution to improve the surface dependent properties like wear, corrosion and oxidation resistance involves tailoring the surface composition and/or micro-structure of the near-surface region of a component without affecting the bulk. This may be achieved, using a high power laser beam as a source of heat, by surface hardening, melting, alloying and cladding. Fast heat-ing /cooling rate (104-1011 K/s), very high thermal grad-ient(106-108 K/m)and ultra-rapid resolidification veloc-ity (1-30 m/s) are the characteristics of this process which often develop exotic microstructures and composit-ions having large extension of solid solubility and meta-stable or even amorphous phases in the surface. This paper gives a brief review of the present status and future scope of laser assisted surface engineering with parti-cular reference to the authors' work

Two new μ2-(1,1-azido) and μ2-(1,1-phenoxido)-bridged dinuclear nickel(II) complexes: Syntheses, single-crystal structures and magnetic studies

Two dinuclear azido bridged Ni(II) complexes [Ni2(HL1)2(N3)(C8H7O3)]∙(H2O) (1) and [Ni2(L2)2(N3)2(H2O)](2) [H2L1 and HL2 are Schiff bases, obtained from the condensation of 2-hydroxy-3-methoxy-benzaldehyde with 2-amino-2-methyl-1-propanol and N,N-diethylethylene diammine, respectively; C8H7O3 = 3-methoxy-2-oxo-benzaldehyde] have been synthesized and their crystal structures have been determined. Complex 1, C32H39N5Ni2O10, crystallizes in a triclinic system, space group P-1 with a = 10.0846(6), b = 12.5179(7), c = 14.1176(8) Å, α = 74.3873(7), β =83.9553(7), γ = 83.1921(7) º and Z = 2; complex 2, C28H44N10Ni2O5 , crystallizes in an orthorhombic system, space group Pbca with a = 12.4197(1), b = 21.4737(4), c = 24.4569(5) Å, and Z = 8. X-ray single crystal structure determination reveals that both the complexes are dinuclear with μ2-(1,1-azido) and μ2-(penoxido) bridges. Variable temperature magnetic studies indicate overall ferromagnetic interaction between nickel(II) centers in both the complexes. The experimental magnetic data of the complexes were fitted using PHI program and isotropic Hamiltonian H = -JS1S2, where S1 = S2 = SNi. A zero-field splitting parameter (D) and intermolecular interaction term (zJ') were also considered in the model and a good agreement between experimental and simulated curves were found by using the following parameters: gNi= 2.13, DNi= 5.83 cm-1, JNi-Ni = 14.61 cm-1 and zJ' = -0.1 cm-1 for 1, and gNi= 2.15, DNi= 2.33 cm-1, JNi-Ni = 13.09 cm-1and zJ' = -0.07 cm-1 for 2

Weighted Scale-free Networks in Euclidean Space Using Local Selection Rule

A spatial scale-free network is introduced and studied whose motivation has been originated in the growing Internet as well as the Airport networks. We argue that in these real-world networks a new node necessarily selects one of its neighbouring local nodes for connection and is not controlled by the preferential attachment as in the Barab\'asi-Albert (BA) model. This observation has been mimicked in our model where the nodes pop-up at randomly located positions in the Euclidean space and are connected to one end of the nearest link. In spite of this crucial difference it is observed that the leading behaviour of our network is like the BA model. Defining link weight as an algebraic power of its Euclidean length, the weight distribution and the non-linear dependence of the nodal strength on the degree are analytically calculated. It is claimed that a power law decay of the link weights with time ensures such a non-linear behavior. Switching off the Euclidean space from the same model yields a much simpler definition of the Barab\'asi-Albert model where numerical effort grows linearly with $N$.Comment: 6 pages, 6 figure

Initiation sites for discontinuous precipitation in some Cu-base alloys

A systematic effort has been made to investigate the suitability of various interfaces, natural as well as artificial, to initiate discontinuous precipitation. The interfaces studied in the present investigation include sample surface (external), and grain and interphase boundaries. It has been demonstrated that in addition to grain boundaries, non-conventional initiation sites like coherent faces of a twin or eutectic/eutectoid boundaries under favourable conditions may also nucleate discontinuous precipitation. In general, the ability of an interface to undergo thermally activated migration appears to be the most important criterion for the initiation of discontinuous precipitation

Mathematical modelling of peritectic transformation in binary systems

A simple diffusional analysis of peritectic transformat-ion based on the linearized concentration gradient approximation and a rigorous numerical model of the peri-tectic transformation as well as the solid state homo-genization process following liquid depletion has been presented.The overall and interface mass balance equations are utilized to calculate the rate of movement of the interfaces in the finite geometry. The predictions of the present models, show a better agreement with the experi-mentally determined kinetic data from the Cd-Ag and Pd-Bi systems as compared to those by the earlier proposed 'models based on quasi-static interface or time-invariant or Laplacian concentration profiles. However, the computed kinetics differ from the observed rates of transformation at a later stage (-50% transformation), perhaps, due to the deviation from the idealized cell configuration consi-dered in the calculations

A nonlinear Schr\"odinger equation for water waves on finite depth with constant vorticity

A nonlinear Schr\"odinger equation for the envelope of two dimensional surface water waves on finite depth with non zero constant vorticity is derived, and the influence of this constant vorticity on the well known stability properties of weakly nonlinear wave packets is studied. It is demonstrated that vorticity modifies significantly the modulational instability properties of weakly nonlinear plane waves, namely the growth rate and bandwidth. At third order we have shown the importance of the coupling between the mean flow induced by the modulation and the vorticity. Furthermore, it is shown that these plane wave solutions may be linearly stable to modulational instability for an opposite shear current independently of the dimensionless parameter kh, where k and h are the carrier wavenumber and depth respectively

Mechanism and kinetics of type II discontinuous coarsening in a Zn-4 at% Ag alloy

Discontinuous coarsening (DC) may succeed discontinuous precipitation (DP) either at the same (DCI) or another temperature (DCII). The present study concerns mechanism and kinetics of DCII in a Zn-4 at% Ag alloy in the range 353-513 K following DP at 393 K for 60 h. DCII colonies prefer to initiate either from one or both sides of the interfaces between the former DP colonies. A suitable comparison of the kinetic data reveals that interlamellar spacing (λ) and steady-state growth velocity (v) values in DCII are significantly different than those in DP. On the other hand, the kinetics of DCIvis-a-vis DCII in terms of λ and v are comparable to each other, though the calculated values of the driving forces between them differ marginally. A detailed kinetic analysis of DCII through the Livingston-Cahn model leads to an underestimation of the activation energy (Q b) of grain boundary chemical diffusion of Ag in Zn-Ag (=30.7 kJ mol-1), whereas the same obtained from the modified Petermann-Hornbogen model (=61.0 kJ mol-1) compares well with that for DP/DCI (reported elsewhere by us), and grain boundary self diffusion of Zn. Considering thatQ b in DCII is nearly 50% of the activation energy for volume/matrix diffusion of Ag in Zn, it appears that DCII in the present alloy is a boundary diffusion controlled process