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991.
Abdominal Radiology - Role of acoustic radiation force impulse (ARFI) elastography, in transplant setting, is not well established. We aimed to define the normal mean values of the liver stiffness...  相似文献   
992.
Hydrogen energy holds tremendous promise as a new clean energy option. It is a convenient, safe, versatile fuel source that can be easily converted to the desired form of energy without releasing harmful emissions. Hydrogen storage, which spans both hydrogen production and hydrogen applications, plays a critical role in initiating a hydrogen economy. Apart from the traditional methods used for hydrogen storage, Mg metal has been considered to be the most suitable candidate for application as a safe hydrogen storage material. However, Mg still has several technical problems that must be solved before such an attractive light metal can be considered for use in real applications. This review article aims to present and discuss the most recent research activities (2010–2018) that have been undertaken at the Kuwait Institute for Scientific Research (KISR) to develop and implement new categories of MgH2-based nanocomposites. Comparisons between different catalytic agents used to enhance MgH2 properties are presented and discussed in terms of structure, morphology, thermal stability, and kinetics.

Photos taken in November 2018 at NAM-EBRC, KISR, presenting the successful application of the use of a solid-state hydrogen storage nanocomposite for charging 8 batteries of an electric golf cart, using a 1000 W PEM-fuel cell.  相似文献   
993.
OBJECTIVES: The purpose of this paper is to examine the incidence and determinants of permanent complete heart block (CHB) after nonsurgical septal reduction therapy (NSRT), and to evaluate the clinical impact of permanent pacemaker (PPM) placement. BACKGROUND: Nonsurgical septal reduction therapy with ethanol improves the clinical and hemodynamic parameters in patients with symptomatic hypertrophic obstructive cardiomyopathy. Complete heart block is a common complication after NSRT. METHODS: The database of 261 consecutive patients who underwent NSRT at Baylor College of Medicine was reviewed. Clinical variables that were considered as possible determinants for CHB after NSRT were: age, gender, New York Heart Association (NYHA) functional class, left ventricular outflow tract (LVOT) gradient at rest or with provocation, septal thickness, and baseline exercise duration. For electrocardiographic (ECG) variables, the presence of first-degree atrioventricular (AV) block, bifascicular block, left bundle branch block, atrial fibrillation, and left ventricular hypertrophy were analyzed. In addition, the volume of ethanol injected, the method of administration of ethanol (i.e., bolus vs. slow injection [over 30 to 60 s]), number of septal arteries occluded, use of myocardial echocardiography, and infarct size as determined by peak creatine kinase level. RESULTS: Of 261 consecutive patients, 37 had PPM or automatic implantable cardiac defibrillator placed before NSRT. Of the remaining 224 patients, 31 (14%) developed CHB after the procedure. Multivariate logistic regression analysis showed that female gender (odds ratio [OR] 4.3; P = 0.02), bolus injection of ethanol (OR 51; P = 0.004), injecting more than one septal artery (OR 4.6; P = 0.016), the presence of left bundle branch block (OR 39; P = 0.002), and first-degree AV block (OR 14; P = 0.001) on the baseline ECG are independent predictors of CHB after NSRT. Patients requiring PPM placement had a similar improvement in their NYHA functional class, septal thickness reduction, LVOT gradient reduction, and improvement of exercise capacity when compared with patients who did not require pacing. CONCLUSIONS: Multiple demographic, electrocardiographic, and technical factors seem to increase the risk of CHB after NSRT. Patients with CHB after NSRT derive similar clinical and hemodynamic benefit to patients who did not require permanent pacing.  相似文献   
994.
This is a case of refractory vasospastic angina with unusual electrocardiographic findings and rare coronary angiographic documentation of diffuse spasm of the left coronary system with a baseline of near normal coronary arteries. A 66-year-old man presented with severe vasospastic angina that eventually progressed to non-ST elevation myocardial infarction (NSTEMI). During the episodes of chest pain, the electrocardiogram revealed ST segment depression rather than elevation. Coronary angiography revealed near normal coronary arteries with initial diffuse spasm of the left coronary system. The patient continues to be symptomatic despite treatment with different forms and doses of nitrates and calcium channel blockers. No financial support was needed or provided by any source.  相似文献   
995.
Formation of a new metastable fcc-MgH2 nanocrystalline phase upon mechanically-induced plastic deformation of MgH2 powders is reported. Our results have shown that cold rolling of mechanically reacted MgH2 powders for 200 passes introduced severe plastic deformation of the powders and led to formation of micro-lathes consisting of γ- and β-MgH2 phases. The cold rolled powders were subjected to different types of defects, exemplified by dislocations, stacking faults, and twinning upon high-energy ball milling. Long term ball milling (50 hours) destabilized β-MgH2 (the most stable phase) and γ-MgH2 (the metastable phase), leading to the formation of a new phase of face centered cubic structure (fcc). The lattice parameter of fcc-MgH2 phase was calculated and found to be 0.4436 nm. This discovered phase possessed high hydrogen storage capacity (6.6 wt%) and revealed excellent desorption kinetics (7 min) at 275 °C. We also demonstrated a cyclic-phase-transformation conducted between these three phases upon changing the ball milling time to 200 hours.

Effect of mechanically-induced cold-rolling followed by high energy ball milling on cyclic phase transformation.

The worldwide interest in MgH2 is attributed to the natural abundance of Mg metal, and its capability to store hydrogen up to 7.60 wt% (0.11 kg H2 L−1).1–3 Among the metal hydride family, MgH2 has been considered as a promising candidate for solid-state hydrogen storage.4–6 Despite the attractive properties of MgH2, and the simplicity for producing the compound on an industrial scale at ambient temperature via a reactive ball milling (RBM) technique,7,8 MgH2 is a very stable compound, and possesses slow kinetics of hydrogenation and dehydrogenation under 300 °C.9 Since the 1990s efforts have been made in order to destabilize MgH2 and improve its hydrogenation and dehydrogenation kinetics upon doping with a long list of catalysts.10–15 Most of the used catalysts showed significant enhancement of the kinetics behavior for MgH2, indexed by a decreasing decomposition temperature and a speed-up of its kinetics behavior.16–20 In spite of the beneficial effects obtained upon adding such foreign catalytic agents, they always lead to a dramatic decrease of the hydrogen storage capacity of MgH2.21,22Apart from doping MgH2 powders with catalysts, it has been experimentally demonstrated by some authors that changing the crystal structure of stable β-tetragonal MgH2 phase to a less stable phase of γ-orthorhombic MgH2 led to improve the gas uptake/release kinetics and decrease the hydrogenation temperature without drastic decreasing of the storage capacity.23–26 The β-to-γ phase transformations can be attained via severe plastic deformation (SPD)27 at ambient temperature by different approaches such as high-energy ball milling (HEBM),28 cold rolling (CRing),29 equal channel angular pressing (ECAP),30 and high pressure torsion (HPT).22,31 A common result of these employed techniques is the formation of nanocrystalline phase along with introducing high intensity defects, leading to increase of grain boundaries density. Presence of these defects in the lattice leads to create nucleation points for hydrogenation, where existence of large number of grain boundaries assists fast diffusion pathways for hydrogen.The present work has been addressed in part to study the effect of HEBM on the structure and decomposition properties of CRed MgH2 powders. Moreover, we aimed to investigate experimentally the possibility of formation a new metastable MgH2 phase rather than the reported g-phase and theoretically calculated δ and ε phases32 upon long term of milling.For the purpose of the present study, 5 g Mg (∼80 μm, 99.8 wt%) powder was balanced inside a He gas atmosphere-glove box and sealed together with fifty hardened steel-balls (11 mm in diameter), using ball-to-powder weight ratio as 40 : 1. The vial was then evacuated to the level of 10−3 bar and then filled with 50 bar of H2. The RBM process was carried out at room temperature, using planetary-type HEBM. After 25 hours (h) of RBM, the vial was open inside the glove box to discharge the powders. The powders were charged and sealed in a stainless steel (SUS304) tube (0.8 cm diameter and 20 cm length) inside the glove box. The tube contained MgH2 powders were severely CRed for different number of passes (1 to 200 passes), using two-drum type manual cold roller (11 cm wide × 5.5 cm rollers diameter). The as-CRed powders for 200 passes were then HEBMed under hydrogen gas for different milling time, in the range between 3 h to 50 h. All the samples were characterized by means of X-ray diffraction (XRD) with Cu radiation, field-emission high-resolution transmission electron microscope (FE-HRTEM) equipped with energy-dispersive X-ray spectroscopy (EDS), field emission scanning electron microscope (FE-SEM)/EDS, and differential scanning calorimeter (DSC). The absorption/desorption kinetics were investigated via Sievert''s method in different temperatures under hydrogen gas pressure in the range between 200 mbar to 8 bar.The XRD patterns of MgH2 powders obtained after 25 h of RBM is shown in Fig. 1a. Bragg peaks corresponding to starting hcp-Mg powders were hardly seen and replaced by sharp diffracted lines related to γ- and β-MgH2 phases, as elucidated in Fig. 1a. The SEM observations indicated the powders tendency to agglomerate, forming large aggregates upon CRing for 25 passes (Fig. 2a). Increasing the CRing passes to 200 times led to grain refinement, as implied by the broadening in the Bragg-peaks presented in Fig. 1b. At this stage, micro-bands with thickness of 143 μm were developed as a result of cold working generated during CRing process, as shown in Fig. 2b. The FE-HRTEM image of as-CRed powders for 200 passes indicated the development of lattice imperfections (e.g. stacking faults and deformation twins). This is implying the mechanically-induced SPD, as elucidated in ESI, Fig. S1.Open in a separate windowFig. 1XRD patterns of MgH2 powders obtained after 25 h of RBMing (a), and then CRed for 200 passes (b). XRD pattern of CRed powders for 200 passes and then HEBMEd for 50 h is presented in (c).Open in a separate windowFig. 2FE-SEM micrographs taken at accelerated voltage of 1 kV of MgH2 powders obtained after 25 h of RBMing and then CRed for (a) 25, and (b) 200 passes.In order to study the effect of HEBM on the stability of cold-rolled MgH2 aggregates, the powders were charged into tool steel vial and ball milled under 50 bar of H2 for different milling time. The XRD pattern of CRed MgH2 powders obtained after 200 CR passes and then HEBMed for 50 h is displayed in Fig. 1c. Obviously, the Bragg peaks corresponding to γ- and β-MgH2 phases were completely vanished and replaced by new Bragg peaks of unreported phase, appeared at scattering angles (2θ) of, 35.034, 40.584, 58.758, 70.115, and 73.868 (Fig. 1c). XRD analysis indicated that this discovered MgH2 phase has face centered cubic structure (fcc) of space group, Fm3̄m(225). The lattice parameter (ao) of this phase, calculated from (111) was 0.44361 nm. The as-synthesized fcc-MgH2 powders had fine spherical particles with sizes distributed in the range between 0.25 μm to 1 μm, as displayed in Fig. 3.Open in a separate windowFig. 3FE-SEM micrograph of MgH2 powders obtained after 25 h of RBM, CRed for 200 passes and finally HEBMed for 50 h.
Peak position, 2θ (degree)Interplanar spacing, d (nm)Miller indexes (h,k,l)Lattice parameter, ao (nm)
35.0340.256121110.44361
40.5840.222292000.44458
58.7580.157132200.44443
70.1150.134213110.44512
73.8680.128292220.44441
Open in a separate windowThe FE-HRTEM image of the as-CRed powders for 200 passes and then HEBMed for 50 h is shown in Fig. 4. The image revealed Moiré fringe image for 3 intimated nanograins. Filtered-fringe images corresponding to Zone I is presented in Fig. 4a. The d-spacing related to fcc-MgH2 (111) was calculated and found to be 0.2559 nm, where the corresponding ao was calculated and found to be 0.4433 nm. These values matches well with the XRD analysis (Fig. 4c, was taken from Zone I and oriented to [001] axis, where the corresponding FFT showed spot-electron diffraction pattern related to fcc-MgH2 (111).Open in a separate windowFig. 4(a) FE-HRTEM image, (b) filtered atomic resolution image of Zone I, and (c) FFT image of MgH2 powders obtained after 25 h of RBM, consequently CRed for 200 passes and finally HEBMed for 50 h. Fig. 5 presents DSC thermograms of MgH2 powders obtained after 25 h of RBM, consequently cold-rolled for 200 passes and then HEBM for different times, as indexed in Fig. 5. The DSC curves for the powders obtained after 25 h of RBM and then cold-rolled only without milling for different passes are shown together in ESI (Fig. S2).Open in a separate windowFig. 5DSC thermograms of MgH2 powders obtained after 25 h of RBM, consequently CRed for 200 passes and final HEBMed for different milling times (6 h to 50 h). The values related to the peak temperatures for each milling time is elucidated in each curve.The decomposition temperature of the powders obtained after 25 h of RBM (before applying CRing process) was 415 °C (Fig. S2), and tended to decrease sharply to 361 °C upon powders CRing for 200 passes, as displayed in Fig. S2. This significant decreasing on the decomposition temperature upon increasing the number of CRing passes was attributed to destabilization of MgH2, yielded from introducing severe plastic deformation to the powders.The XRD pattern for MgH2 powders obtained after 200 CRing passes and then heated in DSC up to 500 °C showed the presence of a single hcp-Mg phase (Fig. S3). The as-HEBMed of the powders CRed for 200 passes revealed single endothermic events related to the decomposition reaction (Fig. 5).Obviously, the peak temperature of the samples obtained after different milling times shifted monotonically to the low temperature side with increasing the HEBMing time (Fig. 5). After 50 h of milling (single metastable fcc-MgH2 phase), the decomposition temperature was reordered to be 222 °C (Fig. 5). This temperature was far below the corresponding decomposition temperature (361 °C, Fig. S3) corresponding to as-CRed powders (γ- + β-MgH2 phases) obtained after 200 passes (Fig. S3).The powders obtained after 50 h of HEBM was annealed in the DSC at 220 °C (just beyond decomposition onset temperature) and at 375 °C (well above the onset decomposition temperature) for 7 min. XRD pattern of the first sample annealed at 220 °C indicated metastable fcc-MgH2-to-stable β-MgH2 phase transformation, as implied by disappearance of fcc-Bragg peaks and the presence of pronounced sharp Bragg lines corresponding to β-MgH2 coexisted with small volume fraction of γ-MgH2 (Fig. 6a).Open in a separate windowFig. 6XRD patterns of the samples obtained after 50 h and then annealed in the DSC for 7 min at (a) 220 °C, and (b) 375 °C for 7 min.FE-HRTEM (Fig. 7a) and NBD (Fig. 7b) analysis of the annealed sample at 220 °C confirmed the presence of γ- and β-MgH2 phases and a complete disappearance of metastable fcc-MgH2, as displayed in Fig. 7a and b, respectively. In contrast, XRD pattern of the sample annealed at 375 °C showed the Bragg peaks of hcp-Mg coexisted with small volume fraction of undecomposed β-MgH2 crystals (Fig. 6b). It can be concluded from the structural and thermal analysis that γ- and β-MgH2 phases tended to transform to a new metastable phase upon CRing for 200 passes followed by HEBMing for 50 h. The obtained metastable fcc-MgH2 phase transformed into more stable phases of γ- and β-MgH2 phases when annealed at 220 °C for 7 min. A complete phase transformation to hcp-Mg was attained upon annealing fcc-MgH2 at 375 °C.Open in a separate windowFig. 7(a) FE-HRTEM, and (b) NBDP of the sample milled for 50 h and then annealed in the DSC at 220 °C for 7 min.Further experiments were conducted to examine the stability of fcc-MgH2 phase against the mechanical deformation generated by HEBMing. The powders obtained after 50 h were continuously milled for 100 h, 150 h, and 200 h. The XRD pattern of the milled powders for 100 h indicated the disappearance of Bragg peaks related fcc-MgH2 phase, which were replaced by diffracted lines related to γ- and β-MgH2 phases as shown in Fig. 8a. This implies the disability of fcc-MgH2 phase to withstand against the shear and impact forces generated by the milling media. Surprisingly, increasing the HEBMing to 150 h led to clear γ- , β-MgH2 to fcc-MgH2 (less stable phase) phase transformation (Fig. 8b). This is indicated by the presence of Bragg peaks related to fcc-MgH2 phase and the disappearance of the diffracted lines corresponding to the MgH2 phases, as displayed in Fig. 8b.Open in a separate windowFig. 8XRD patterns of as-CRed MgH2 powders for 200 passes and then HEBMed for (a) 100 h, (b) 150 h, and (c) 200 h. Fig. 9 presents a schematic illustration of free energy changes of β-γ-fcc MgH2 phases upon increasing HEBM time. Based on the results motivated of the present study, mechanically-induced fcc-MgH2 to γ- and β-MgH2 phase transformation (point 3-to-points 2 + 3) was achieved upon increasing the milling time to 100 h. Introducing severe lattice imperfections to the fcc-phase is proposed to be responsible to insist this metastable phase to gain free energy and hence transformed into a more stable phase, as illustrated in Fig. 9. This phase transformation can be taken place upon annealing the powders via thermally induced phase transformation, as indexed by point 3-to-points 2 + 1 (Fig. 9).Open in a separate windowFig. 9Schematic presentation of free energy changes conducted upon HEBMing CRed MgH2 powders for long term of milling.The obtained γ- and β-MgH2 composite phases were subjected plastic deformation and defects, leading to lose free energy and transformed to the same metastable fcc-MgH2 phase with further milling time (150 h), as denoted by points 1 + 2 to point 3 (Fig. 9). Further increasing the milling time (200 h) led fcc-MgH2 to gain energy and failed into more stable phases of γ- and β-MgH2.Since high-energy ball milling process introduces intensive vacancies, lattice defects, grain boundaries and surfaces, the ball-milled powders can store a large amount of mechanical-strain energy.33,34 Introducing such defects to the crystalline lattice destroys the periodical structure of the stable tetragonal-MgH2 phase, leading to the formation of a less stable phase (fcc-MgH2). Moreover, the present result suggests that the formation enthalpy of the metastable fcc-MgH2 phase is comparable to the γ- and β-MgH2 phases and the energy barrier between these three phases is probably rather low to allow such cyclic-phase transformations. We should emphases that all the results obtained from XRD analysis were used to determine the weight percentage of each phase, using the approaches described by Guan et al.,35 Ma et al.,36 Yu et al.,37 and Cheng et al.38 Fig. 10 displays the dehydrogenation kinetics behaviors of the CRed powder obtained after 200 passes and then HEBMed for 50 h (fcc-MgH2 phase). The measurements were conducted in the temperature range of 175 °C to 275 °C under 200 mbar.Open in a separate windowFig. 10Dehydrogenation kinetics measured for 10 individual samples of MgH2 powders obtained after 25 h of RBM, consequently CRed for 200 passes and then HEBMed for 50 h. The measurements were conducted under 200 mbar H2 (a) without powders activation, and (b) after activated the powders at 300 °C under 10 bar H2.In order to maintain the crystal structure of the powders (fcc-MgH2 phase) obtained after this stage of milling, the desorption kinetics measurements measured without activation for 5 individual samples (Fig. 10a). All samples were successfully desorbed their hydrogen storage with different time scale. Generally, the fcc-MgH2 powders showed advanced dehydrogenation characteristics over γ- and β-MgH2 phases. At 175 °C, the sample desorbed ∼4 wt% H2 within 40 min (Fig. 10a). However, the powders desorbed about 6.5 wt% H2 within 22 min at 200 °C (Fig. 6a). Increasing the applied temperature to 225 °C and 250 °C, improved the dehydrogenation kinetics of fcc-MgH2, indicated by the short time required to desorb 6.6 wt% H2 in 17 min and 10 min, respectively (Fig. 10a).Outstanding desorption kinetics was conducted at 275 °C, when the sample desorbed 6.6 wt% H2 within 7 min, as elucidated in Fig. 10a. We should emphases that the XRD patterns for the examined samples at temperature range laid between 175 °C to 225 °C revealed presence of Bragg peaks corresponding to γ- and β-MgH2 phases. However, the XRD pattern for those samples examined at higher temperatures (250 °C and 275 °C) revealed diffracted lines of hcp-Mg phase. Fig. 10b displays the dehydrogenation kinetics conducted for the same samples shown in 10a, however, they were activated firstly at 300 °C (far above the transformation temperature of fcc-MgH2 to γ- and β-MgH2 phases) under 25 bar H2. Based on this activation step condition, all the samples lost their fcc-structure and completely transformed into γ- and β-MgH2 phases. This led to a significant deduction of dehydrogenation kinetics that become very slow when compared with the same samples shown in Fig. 10a. For example, the sample examined at 175 °C required more than 650 min to desorb less than 5.5 wt% H2 (Fig. 10b). The two samples examined at 200 °C and 225 °C desorbed about 6.4 and 6.6 wt% H2 within 600 and 390 min, respectively (Fig. 10b). Comparing the necessary desorption time (100 min) for the sample examined at 275 °C to release 6.6 wt% H2 (Fig. 10b) with that time required (7 min) for fcc-MgH2 sample (Fig. 10a) to desorb same hydrogen amount at the same temperature, we can realize that the kinetics desorption of fcc-MgH2 phase is 14 time faster than γ- and β-MgH2 phases.  相似文献   
996.
Intravenous versus Oral Acetaminophen for Pain: Systematic Review of Current Evidence to Support Clinical Decision-Making     
Farah Jibril  Sherif Sharaby  Ahmed Mohamed  Kyle J Wilby 《The Canadian journal of hospital pharmacy》2015,68(3):238-247

Background:

Intravenous (IV) acetaminophen is increasingly used around the world for pain control for a variety of indications. However, it is unclear whether IV administration offers advantages over oral administration.

Objective:

To identify, summarize, and critically evaluate the literature comparing analgesic efficacy, safety, and pharmacokinetics for IV and oral dosage forms of acetaminophen.

Data Sources:

A literature search of the PubMed, Embase, and International Pharmaceutical Abstracts databases was supplemented with keyword searches of Science Direct, Wiley Library Online, and Springer Link databases for the period 1948 to November 2014. The reference lists of identified studies were searched manually.

Study Selection and Data Extraction:

Randomized controlled trials comparing IV and oral dosage forms of acetaminophen were included if they assessed an efficacy, safety, or pharmacokinetic outcome. For each study, 2 investigators independently extracted data (study design, population, interventions, follow-up, efficacy outcomes, safety outcomes, pharmacokinetic outcomes, and any other pertinent information) and completed risk-of-bias assessments.

Data Synthesis:

Six randomized clinical trials were included. Three of the studies reported outcomes pertaining to efficacy, 4 to safety, and 4 to pharmacokinetics. No clinically significant differences in efficacy were found between the 2 dosage forms. Safety outcomes were not reported consistently enough to allow adequate assessment. No evidence was found to suggest that increased bioavailability of the IV formulation enhances efficacy outcomes. For studies reporting clinical outcomes, the results of risk-of-bias assessments were largely unclear.

Conclusions:

For patients who can take an oral dosage form, no clear indication exists for preferential prescribing of IV acetaminophen. Decision-making must take into account the known adverse effects of each dosage form and other considerations such as convenience and cost. Future studies should assess multiple-dose regimens over longer periods for patients with common pain indications such as cancer, trauma, and surgery.  相似文献   
997.
Synthesis of Some 1,4,6‐Trisubstituted‐2‐oxo‐1,2‐dihydropyridine‐3‐carbonitriles and Their Biological Evaluation as Cytotoxic and Antimicrobial Agents          下载免费PDF全文
Hassan M. Faidallah  Sherif A. F. Rostom  Mona H. Badr  Azza E. Ismail  Ameen M. Almohammadi 《Archiv der Pharmazie》2015,348(11):824-834
  相似文献   
998.
Inactivation of Middle East respiratory syndrome‐coronavirus in human plasma using amotosalen and ultraviolet A light          下载免费PDF全文
Salwa I. Hindawi  Anwar M. Hashem  Ghazi A. Damanhouri  Sherif A. El‐Kafrawy  Ahmed M. Tolah  Ahmed M. Hassan  Esam I. Azhar 《Transfusion》2018,58(1):52-59
  相似文献   
999.
Imaging and staging of neuroendocrine cervical cancer     
Elsherif  Sherif  Odisio  Erika G. L. C.  Faria  Silvana  Javadi  Sanaz  Yedururi  Sireesha  Frumovitz  Michael  Ramalingam  Preetha  Bhosale  Priya 《Abdominal imaging》2018,43(12):3468-3478
  相似文献   
1000.
Molecular Basis of Crystal Morphology-Dependent Adhesion Behavior of Mefenamic Acid During Tableting     
Vrushali Waknis  Elza Chu  Roxana Schlam  Alexander Sidorenko  Sherif Badawy  Shawn Yin  Ajit S. Narang 《Pharmaceutical research》2014,31(1):160-172

Purpose

The molecular basis of crystal surface adhesion leading to sticking was investigated by exploring the correlation of crystal adhesion to oxidized iron coated atomic force microscope (AFM) tips and bulk powder sticking behavior during tableting of two morphologically different crystals of a model drug, mefenamic acid (MA), to differences in their surface functional group orientation and energy.

Methods

MA was recrystallized into two morphologies (plates and needles) of the same crystalline form. Crystal adhesion to oxidized iron coated AFM tips and bulk powder sticking to tablet punches was assessed using a direct compression formulation. Surface functional group orientation and energies on crystal faces were modeled using Accelrys Material Studio software.

Results

Needle-shaped morphology showed higher sticking tendency than plates despite similar particle size. This correlated with higher crystal surface adhesion of needle-shaped morphology to oxidized iron coated AFM probe tips, and greater surface energy and exposure of polar functional groups.

Conclusions

Higher surface exposure of polar functional groups correlates with higher tendency to stick to metal surfaces and AFM tips, indicating involvement of specific polar interactions in the adhesion behavior. In addition, an AFM method is identified to prospectively assess the risk of sticking during the early stages of drug development.  相似文献   
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