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With the popularization of electricity, the use of electric porcelain is becoming more and more extensive, but in the process of production, the waste of electric porcelain continues to accumulate and increase, which not only pollutes the environment but also affects the normal life of human beings. Therefore, it is urgent to deal with these electric porcelain wastes. In this paper, the electric ceramic waste is used as the main raw material, and starch and kaolin are added to optimize the formula to prepare porous ceramsite. The effects of the content of electrical ceramic waste, sintering temperature and holding time on the properties of porous ceramsite were studied. After research, the results show that with the increase of waste content, the porosity and water absorption first decrease and then increase, while the compressive strength first increases and then decreases. With the increase of the sintering temperature, the porosity and the water absorption rate decrease continuously at the beginning, and the compressive strength increases continuously at the beginning, but when the sintering temperature increases continuously, there will be a turning point or a flattening point. With the continuous extension of the holding time, the water absorption and porosity continue to increase, while the compressive strength continues to decrease, but the overall change is small. The optimization can be found that when the waste content is 75%, the sintering temperature is 1200 °C, and the holding time is 30 min, the prepared porous ceramsite has the best performance. Its water absorption rate: 13.87%, porosity: 27.52%, compressive strength: 20.06MPa.

With the popularization of "sponge city" in the whole country, the use of permeable bricks is increasing every year. Although the raw materials required for the preparation of permeable bricks are widely sourced, there are few reports on the process of using refractory waste to prepare permeable bricks. It is the ball milling process of refractory waste. The effects of ball milling time, ball mill rotation speed, and ball-to-material ratio on the properties of refractory waste were mainly studied. Through the experimental results and analysis, the following conclusions can be drawn: with the increase of ball milling time, ball milling speed and ball-to-material ratio, the particle size of refractory waste powder gradually decreases. Through research, it is concluded that the optimal ball milling time is 4h, the ball milling speed is 100r/min, and the ball-to-material ratio is 2:1.

Laplace Transform is often used in solving the free vibration problems of structural beams. In existing research, there are two types of simplified models of continuous beam placement. The first is to regard the continuous beam as a single-span beam, the middle bearing of which is replaced by the bearing reaction force; the second is to divide the continuous beam into several simply supported beams, with the bending moment of the continuous beam at the middle bearing considered as the external force. Research shows that the second simplified model is incorrect, and the frequency equation derived from the first simplified model contains multiple expressions which might not be equivalent to each other. This paper specifies the application method of Laplace Transform in solving the free vibration problems of continuous beams, having great significance in the proper use of the transform method.

Topographies of a bioactive glass (45S5 type Bioglass(R)) during 0-4 h of immersion in a supersaturated calcifying solution (SCS) and the SCS containing recombinant porcine amelogenin rP172 (SCS(rP172)) were observed by atomic force microscopy. Other techniques including X-ray diffraction, scanning electron microscopy coupled with energy dispersive X-ray spectroscopy, and transmission electron microscopy were used for some complementary microstructural investigations. The smooth Bioglass surface changed to be very rough after 0.5 h of SCS immersion because of glass network dissolution. Spherical silica-gel particles with diameters of 150-300 nm consisting of substructures of 20-60 nm across had formed on the sample surfaces after 1 h of SCS immersion. The chemisorption of amorphous calcium phosphate and crystallization of nanophase apatite were seen to occur epitaxially on the silica-gel structures during 1-4 h of SCS immersion. During the first 0.5 h of SCS(rP172) immersion, more than 95% of rP172 protein in solution was adsorbed onto the sample surfaces and generated spherical assemblies of 10-60 nm diameters. During 0.5-4 h of SCS(rP172) immersion, the protein assemblies of rP172 remarkably induced the formation of orientated silica-gel plates (approximately 100-nm wide and 50-nm thick) and subsequently of long and thin apatite needle crystals. The recombinant amelogenin rP172-modulated apatite crystals resembled those formed in the early stage of tooth enamel biomineralization, suggesting the functional roles of amelogenins during the oriented growth of enamel crystallites and a great potential for amelogenins in applications designed to fabricate enamel-like calcium phosphate biomaterials.

The effects of a recombinant mouse amelogenin (rM179) on the growth of apatite crystals nucleated on a bioactive glass (45S5 type Bioglass) surface were investigated with a view to gaining a better understanding of the role of amelogenin protein in tooth enamel formation and of its potential application in the design of novel enamel-like biomaterials. Bioglass discs were incubated in phosphate-buffered saline (PBS) to preform a calcium phosphate surface layer and subsequently immersed in blank, bovine serum albumin (BSA)- and rM179-containing supersaturated calcification solutions (SCS(B), SCS(BSA) and SCSrM179), respectively. Calcium phosphate layers formed on all the treated samples and were characterized to be apatite by X-ray diffraction and Fourier transmission infrared spectrophotometry. Under scanning electron microscopy, plate-shaped crystals (approximately 50 nm thick and 300-600 nm across) were observed on the samples after PBS incubation. The crystals grown from SCS(B) were of the typical plate shape except for an increased thickness, while needle-shaped crystals (200-300 nm long and 50-70 nm thick) were precipitated on the SCS(BSA)-immersed samples. Interestingly, it was found that the crystals deposited on the SCSrM179-immersed samples adopted an elongated, curved shape (approximately 500 nm long and approximately 120 nm thick). Further TEM observations showed that the crystals generated by the SCSrM179 immersion appeared to be composed of bundles of lengthwise crystals (15-20 nm thick) orientated parallel to one another, much alike the long and thin crystals observed in the very early stage of enamel formation. The significant modulation by the rM179 protein of apatite crystal growth is quite different from the overall inhibition observed by BSA and most likely is relevant to the specific function of the amelogenin matrix in controlling enamel crystal growth in vivo.

The thermo-reversible transition (clear--opaque) of the amelogenin gel matrix, which has been known for some three decades, has now been clarified by microstructural investigations. A mixed amelogenin preparation extracted from porcine developing enamel matrix (containing "25K," 7.4%; "23K," 10.7%; "20K," 49.5%; and smaller peptides, 32.4%) was dissolved in dilute formic acid and reprecipitated by adjusting the pH to 6.8 with NaOH solution. Amelogenin gels were formed in vitro by sedimenting the precipitate in microcentrifuge tubes. The gels were fixed with Karnovsky fixative at 4 and 24 degrees C, which was found to preserve their corresponding clear (4 degrees C) and opaque (24 degrees C) states. Scanning electron microscopy, atomic force microscopy, and transmission electron microscopy were employed for the microstructural characterization of the fixed clear and opaque gels. The amelogenin gel matrix was observed to possess a hierarchical structure of quasi-spherical amelogenin nanospheres and their assemblies. The nanospheres of diameters 8-20 nm assemble to form small spherical assemblies of diameters 40-70 nm that further aggregated to form large spherical assemblies of 70-300 nm in diameter. In the clear gel, most of the large assemblies are smaller than 150 nm, and the nanospheres and assemblies are uniformly dispersed, allowing an even fluid distribution among them. In the opaque gel, however, numerous spherical fluid-filled spaces ranging from 0.3 to 7 microm in diameter were observed with the majority of the large assemblies sized 150-200 nm in diameter. These spaces presumably result from enhanced hydrophobic interactions among nanospheres and/or assemblies as the temperature increased. The high opacity of the opaque (24 degrees C) gel apparently arises from the presence of the numerous fluid-filled spaces observed compared to the low-temperature (4 degrees C) preparation. These observations suggest that the hydrophobic interactions among nanospheres and different orders of amelogenin assemblies are important in determining the structural integrity of the dental enamel matrix.

Microstructures of non-unions of human humeral shaft fractures were investigated by using scanning electron microscopy, transmission electron microscopy, and X-ray microdiffraction. The non-union has a trabeculae structural framework similar to woven bone. Among the trabeculae are cavities that are subdivided into small chambers by thin plates of collagen fibrils. Some chambers are filled with variously shaped mineralized particles several micrometers in size. The collagen fibrils in both the trabeculae and the thin plates were only slightly mineralized by hydroxyapatite. Vesicles loaded with noncrystalline calcium phosphate (NCP) were observed in most mineralized particles, and brushite crystals with special morphology were seen to be embedded in some particles in irregular shapes. X-ray microdiffraction results indicated that the mineral phases in the non-unions were mainly NCP in addition to small amounts of hydroxyapatite and brushite. NCP deposition and insufficient mineralization of the collagen fibrils may be two important microstructural features of the non-unions of human humeral shaft fractures different from normally repaired bone callus.

Microstructures of the early external callus after diaphyseal fractures of human long bone were investigated by using scanning electron microscopy, X-ray diffraction, and transmission electron microscopy. It was found that the main structural framework of the human early callus consists of disordered, mineralized collagen fibrils with a small fraction of regions of ordered collagen fibrils. X-ray diffraction analyses show that hydroxyapatite containing some carbonate impurity has been the dominant crystalline phase in the human early callus. In addition, a small amount of brushite phase was detected. Selected area diffraction analyses indicated that hydroxyapatite microcrystals were embedded in microfibrils with a diameter of 4.5 nm and well-banded fibrils, whereas brushite particles of 15-20 nm in an irregular shape were located in the noncollagenous organic matter around the nonmineralized, ordered collagen fibrils. The spatial distribution of the brushite particles in the human early callus was for the first time determined. The brushite particles probably serve as the reservoir of calcium and phosphate ions for subsequent mineralized periods rather than the precursor of hydroxyapatite.

Amelogenin proteins constitute the primary structural entity of the extracellular protein framework of the developing enamel matrix. Recent data on the interactions of amelogenin with calcium phosphate crystals support the hypothesis that amelogenins control the oriented and elongated growth of enamel carbonate apatite crystals. To exploit further the molecular mechanisms involved in amelogenin-calcium phosphate mineral interactions, we conducted in vitro experiments to examine the effect of amelogenin on synthetic octacalcium phosphate (OCP) crystals. A 10% (wt/vol) recombinant murine amelogenin (rM179, rM166) gel was constructed with nanospheres of about 10- to 20-nm diameter, as observed by atomic force microscopy. The growth of OCP was modulated uniquely in 10% rM179 and rM166 amelogenin gels, regardless of the presence of the hydrophilic C-terminal residues. Fibrous crystals grew with large length-to-width ratio and small width-to-thickness ratio. Both rM179 and rM166 enhanced the growth of elongated OCP crystals, suggesting a relationship to the initial elongated growth of enamel crystals.

This paper briefly reviews our recent studies, which aimed to investigate the effects of 1) the Ca2+and PO43-ions flow and 2) amelogenins on the lengthwise growth of octacalcium phosphate (OCP), which is a potent precursor of enamel apatite crystal. OCP crystals were grown at 37°C in a dual membrane system under various amount of ionic inflow into a reaction space, using 1) 5-30mM Ca and PO4solutions as ionic sources and 2) extracted bovine amelogenin and recombinant murine amelogenins (rM179, rM166). With an increase in the amount of Ca2+and/or PO43-ions flow, the length of OCP crystal increased, while the width decreased. As a result, the length to width (L/W) ratio of crystal changed from 3 to 95, while the width to thickness (W/T) ratio from 32 to 9. The effect of amelogenins was unique, regardless of the type of amelogenins: Rod-like and prism-like OCP crystals with large L/W (61∼107) and small W/T (1.3∼2.2) ratios were formed in 10% amelogenin gels. In contrast, characteristic ribbon-like OCP crystals grew without protein and with gelatin, albumin, polyacrylamide gel and agarose gel. Specific interaction of amelogenins with OCP crystal was ascribed to the self-assembly property of amelogenin molecules and their hydrophobic nature. It was suggested that ionic flow and amelogenins play some critical roles in the elongated growth of enamel crystals.

In vitro studies on interactions between amelogenins and calcium phosphate crystals are critical for elucidating biomineralization mechanisms of tooth enamel. This work was aimed at investigating the effects of native porcine amelogenins on octacalcium phosphate (OCP) crystal growth in a gelatin gel. We prepared OCP mineral discs by circulating calcium and phosphate solutions on the opposite ends of the gels loaded with 0-2% amelogenin for one week. A dose-dependent modulation of OCP crystal habit by amelogenins was observed by scanning electron microscopy. While the incorporation of 0.125, 0.25, or 0.5% amelogenins showed no significant effect on the crystal morphology, in the presence of I and 2% amelogenins, the crystals were remarkably longer, having an average aspect ratio 3-5 times greater than that of those formed in the control gels. Transmission electron microscopy and atomic force microscopy suggested that amelogenin assemblies selectively blocked b-axial development, resulting in the c-axial elongation of OCP crystals.

This paper is a short review of recent studies, which were undertaken to investigate interactions of amelogenin with octacalcium phosphate (OCP), and apatite. OCP crystals were grown using two independent experimental systems; (a) in a 10% gelatin gel, containing 0-2% amelogenin, where the crystals were formed in a double-diffusion chamber, and (b) in a 10% pure amelogenin gel, where crystal growth took place in between a cation-selective and a dialysis membrane. Apatite crystals were grown from a supersaturated calcifying solution on a bioactive glass in the absence (SCSB) and the presence of amelogenin (SCSrM179). It was found that OCP crystals formed in 10% gelatin gel containing 1-2% amelogenin were longer (3-5 times larger in aspect ratio) than the OCP crystals formed in 10% gelatin without amelogenin. A profound effect was that found in the cation selective membrane system when 10% amelogenin inhibited the growth morphology in a specific manner. Affected crystals had a length to width ratio twice larger than that of control crystals while the width to thickness ratio was about 1/12 of that of the control crystals. Amelogenin promoted the formation of bundles of lengthwise apatite crystals, which were all oriented parallel to their c axes when grown on SCSrM179. It was found that individual apatite crystals within those bundles adopted an elongated, curved shape. The data presented here suggest that amelogenin nanospheres modulate the growth morphology of apatite and OCP crystals and indicate significant functional roles for amelogenin proteins during the in vivo oriented growth of enamel crystallites.

In order to understand further the mechanism of bone fracture repair, and thus to innovate better operative treatment for bone fracture and to design new implant materials for bone repair, microstructures of external periosteal callus (EPC) of repaired femoral fracture in both children and adults were investigated by using a scanning electron microscope, transmission electron microscopy, and an X-ray microdiffractometer. The repair time after the fractures in children and adults is on average 155 and 370 days, respectively. Collagen fibrils making up children's EPC (CEPC) are underdeveloped and insufficiently mineralized by hydroxyapatite (HA), while those from adults' EPC (AEPC) are similar to normal bone. A lot of particles loaded by brushite (DCPD) minerals were found among the collagen fibrils of CEPC. The main mineral phases in CEPC consist of DCPD and HA, while only HA exists in AEPC. Deposition of DCPD minerals could have compensated for the insufficient mineralization of the collagen fibrils of CEPC, thereby making fractured bone repair more rapidly in children than in adults.

Two leafy electromagnetic bandgap (EBG) structures are proposed for ultra-wideband (UWB) simultaneous switching noise (SSN) suppression in power/ground plane pairs. The valid -35 dB suppression bandwidth of the first design is from 218 MHz to 20 GHz, -40 dB suppression bandwidth of the second design is from 369 MHZ to 20 GHz. The simulated and measured results are compared and presented to verify good performance.