环己烷浮游催化法在碳纤维表面生长碳纳米管

以环己烷为碳源、二茂铁为催化剂前躯,采用浮游催化法成功的在碳纤维表面生长了碳纳米管(CNT),制备了多尺度杂化材料CNTs/CF。实验重点考察了反应温度、二茂铁浓度、载气等参数对CNT在纤维表面生长的影响,通过扫描电镜(SEM)、投射电镜(TEM)研究了CNTs/CF的形貌及产物CNT的微观结构。当固定反应温度为820℃、二茂铁-环己烷浓度为2g/100mL时,随着氢气在载气中含量在0～100%范围内变化,产物CNT直径亦有86nm降低至39nm。通过单丝拉伸测试发现,相比初始碳纤维,不同长度的CNTs/CF单纤维强度下降幅度均在10%以内。     

热处理温度对聚酰亚胺基炭纤维结构性能影响

以聚酰亚胺(PI)纤维为前驱体,经800~2800℃连续高温处理,制备出不同性能的聚酰亚胺基炭(石墨)纤维。采用元素分析、SEM、HR-TEM、Raman、纤维强力仪、电阻率仪等分析手段研究热处理温度对炭纤维(CF)元素含量、结构形貌、力学性能、传导性能等方面的影响。结果表明,随着热处理温度的升高,聚酰亚胺基炭纤维中碳含量从78.97%(800℃)提高到99.72%(2 800℃),非碳原子含量降低;聚酰亚胺基炭纤维表面缺陷数目增加且尺寸增大。同时,纤维的微观结构也从二维乱层石墨结构向有序的三维层状结构发展,表现为石墨化程度的提高及石墨微晶尺寸的增大;炭纤维拉伸强度先增加后降低,最大拉伸强度924.4 MPa,断裂伸长率降低,电阻率减小,热导率增加,2 800℃石墨化处理后纤维热导率为228.4 W·m-1·K-1,是800℃处理后的50.4倍。     

塑性树脂/纤维复合材料界面强度检测方法

本工作设计了一种新的针对热塑性树脂的微珠脱粘实验试样制备方法,以PPS/CF复合材料体系为例,通过偏光显微镜(PLM)、扫描电镜(SEM)和单纤维拉伸仪对该方法进行一定评价.结果表明,此种制样方法所制得的试样树脂微球直径即纤维的包埋长度主要分布在250～450μm之间,很容易满足脱粘法l值小于500 μm的要求.最终测得的PPS树脂与CF间的界面的剪切强度为4.21MPa,实验的标准偏差为1.56MPa,说明此方法有较好的可操作性,所得数据较稳定.     

氧化石墨烯/炭纤维复合增强体的制备及对环氧树脂复合材料界面性能影响

为了改善炭纤维/环氧树脂复合材料的界面性能,以对硝基苯胺为原料,通过两步重氮化还原反应,在炭纤维表面共价接枝氧化石墨烯,制备出氧化石墨烯/炭纤维(GO/CF)复合增强体。研究了反应机理,并对改性前后炭纤维表面的化学结构、微观形貌、表面粗糙度、单丝拉伸强度和炭纤维/环氧树脂复合材料的界面性能等进行了测试分析。结果表明,接枝GO后,炭纤维表面粗糙度增加了188%,单丝拉伸强度提高了13. 2%,断裂伸长率增加12. 1%,界面黏结强度提高了80. 2%。     

塑性树脂/纤维复合材料界面强度检测方法EI

本工作设计了一种新的针对热塑性树脂的微珠脱粘实验试样制备方法,以PPS/CF复合材料体系为例,通过偏光显微镜(PLM)、扫描电镜(SEM)和单纤维拉伸仪对该方法进行一定评价.结果表明,此种制样方法所制得的试样树脂微球直径即纤维的包埋长度主要分布在250～450μm之间,很容易满足脱粘法l值小于500 μm的要求.最终测得的PPS树脂与CF间的界面的剪切强度为4.21MPa,实验的标准偏差为1.56MPa,说明此方法有较好的可操作性,所得数据较稳定.     

炭纤维/聚四氟乙烯复合材料的摩擦磨损性能

分别采用热空气氧化后经钛酸酯偶联剂处理炭纤维(CF)和氩等离子体处理聚四氟乙烯(PTFE)分散液包覆炭纤维制备CF/PTFE复合材料,研究这两种CF表面改性方法对复合材料拉伸性能及摩擦磨损性能的影响,并采用扫描电子显微镜对试样拉伸断面与磨损表面进行观察和分析。结果表明,热空气氧化后经偶联剂处理炭纤维可使CF/PTFE复合材料的拉伸强度与断裂伸长率分别提高33%和82%、磨损率下降44%,氩等离子体处理PTFE分散液包覆炭纤维可使复合材料的拉伸强度与断裂伸长率分别提高49%和100%、磨损率下降56%。     

气相催化裂解法制备微米级螺旋形炭纤维的研究

以商用乙炔为碳源，镍板为催化剂，含硫化合物为助催化剂，通过气相催化裂解法（VCC）制得了微米级螺旋形炭纤维。通过对影响微螺旋形炭纤维生长因素研究。发现将镍板直立放置于石英管中，可以提高螺旋形炭纤维的收率。同时发现反应温度为710℃～800℃，C2H2/H2=1：3。含硫化合物的流量为1.0mL/min～1.2mL/min时，有利于规整螺旋纤维的生成，通过调节N2的流量，可以获得螺径不同的炭纤维。气体总流量约200mL/min时可制得螺径约4μm的规整炭纤维；气体总流量约150mL/min时可获得螺径约20μm的炭纤维。利用扫描电子显微镜（SEM）考察了螺旋纤维的微观形貌，发现所得的纤维几乎为双螺旋，同时在螺旋纤维生长的先端常观察到由弯曲纳米级纤维形成的绒状物。     

炭纤维增强明胶复合材料的性能研究

制备了不同形式炭纤维增强的明胶复合材料,对不同复合材料的力学性能进行了测量与分析,并对复合材料的拉伸断口进行了观察,研究表明,长炭纤维增强明胶（CL/Gel)复合材料具有最高的拉伸强度,剪切强度和模量,而炭纤维毡增强明胶（CF/Gel)复合材料因内部存在较多的孔隙使其力学性能最差,因此,炭纤维毡不能用于增强明胶材料,由于纺织炭纤维布增强明胶（Cw/Gel)复合材料的纤维维束内亦有孔隙,炭纤维布的增强效果不及长炭纤维。     

CF/PPEK、CF/PPES复合材料高温力学性能研究

采用预浸热压成型工艺制备碳纤维增强杂萘联苯聚醚酮(CF/PPEK)和碳纤维增强杂萘联苯聚醚砜(CF/PPES)单向复合材料试样,通过对试样在常温和高温条件下的力学性能测试与分析,研究了高性能热塑性复合材料在高温条件下力学性能及其强度和模量保留率的变化规律.实验表明,在250℃下其拉伸和弯曲强度及模量的保留率均在60%以上,仍具有极高的承载能力.利用Tr-n预测模型对这两种复合材料高温力学性能进行的预测结果与试验值基本吻合,从而验证了这个模型的可行性.     

不同纺丝工艺T800炭纤维及其缠绕压力容器性能差异性研究（英文）

对比分析了采用不同纺丝工艺制备的T800HB炭纤维与T800SC炭纤维之间的微观形态、NOL环性能、压力容器应变分布及水压实验的性能差异。结果表明,纺丝工艺不同使得T800HB炭纤维较T800SC炭纤维脆性更大,与树脂基体结合更强,导致复合材料拉伸破坏时吸收能量较少而影响其拉伸性能的发挥。采用T800HB炭纤维制备的复合材料压力容器在封头上靠近赤道位置处产生了更高的压缩应变,更易在此处发生低压爆破。Φ150 mm压力容器水压检测结果表明,T800HB炭纤维压力容器由于低压破坏,环向纤维强度发挥率仅为72%,容器特性系数为34.8 km;而T800SC炭纤维压力容器环向纤维强度发挥率达92.3%,容器特性系数达47.2 km。因此,采用干喷湿纺工艺所制T800SC炭纤维更适合缠绕工艺制备压力容器。     

短切炭纤维增强沥青基C/C复合材料的组织特征

利用新型、高效的模压半炭化成型工艺，在大气环境下制备出了短切炭纤维增强沥青基C／C复合材料制品，并借助光学显做镜和扫描电镜对其微观组织和断口形貌进行了观察。通过分析，解释了短切炭纤维增强沥青基C／C复合材料中炭纤维损伤的形成机制，提出了作为增强体相的短切炭纤维和焦炭颗粒与基体炭之间独特的界而结构模型。研究还表明：复合材料中明显存在着基体相和颗粒相一基体相的显微结构不仅呈层片状，而且层片状的结构好像数层桔子皮，将颗粒相包裹起来，这种“桔皮包裹”式的结构与炭纤维表面的POG结构基本相似。     

短切炭纤维增强沥青基C/C复合材料的力学性能

利用模压半炭化成型工艺在大气环境下制备出了短切炭纤维增强沥青基C／C复合材料（简称SCFRC）。研究了短切炭纤维的体积分数对SCFRC材料的体积密度和力学性能的影响规律。借助光学显微镜和扫描电镜对其微观组织和断口形貌进行了观察，分析了短切炭纤维对SCFRC材料的增强机制。结果表明，当短切炭纤维的体积分数由0％增大到11．8％时，SCFRC材料的力学性能随之呈线性增加；短切炭纤维增强SCFRC材料的机制主要有裂纹偏转效应、桥联效应以及脱粘和拔出效应。     

Kinetics of chemical vapor infiltration of carbon nanofiber-reinforced carbon/carbon composites

Preforms containing 0, 5, 10, 15 and 20 wt.% carbon nanofibers (CNFs) were fabricated by spreading layers of carbon cloth, and infiltrated by using the technique of isothermal chemical vapor infiltration (ICVI) at the temperature of 1100 °C under the total pressure of 1 kPa and with the flow of the mixture of propane/nitrogen in a ratio of 13:1. The infiltration rates increased with the rising of CNF content, and after 580 h of infiltration, the achievable degree of pore filling was the highest when the CNF content was 5 wt.%, but the composite could not be densified efficiently as the CNF content ranged from 10 to 20 wt.%. An analysis of the results, based on the effective diffusion coefficient and on the in-pore deposition rates, shows that the CNFs, due to their higher aspect ratio, accelerate overgrowth at pore entrances and thus lead to incomplete pore filling.     

Hierarchical carbon nanostructure design: ultra-long carbon nanofibers decorated with carbon nanotubes

Hierarchical carbon nanostructures based on ultra-long carbon nanofibers (CNF) decorated with carbon nanotubes (CNT) have been prepared using plasma processes. The nickel/carbon composite nanofibers, used as a support for the growth of CNT, were deposited on nanopatterned silicon substrate by a hybrid plasma process, combining magnetron sputtering and plasma-enhanced chemical vapor deposition (PECVD). Transmission electron microscopy revealed the presence of spherical nanoparticles randomly dispersed within the carbon nanofibers. The nickel nanoparticles have been used as a catalyst to initiate the growth of CNT by PECVD at 600°C. After the growth of CNT onto the ultra-long CNF, SEM imaging revealed the formation of hierarchical carbon nanostructures which consist of CNF sheathed with CNTs. Furthermore, we demonstrate that reducing the growth temperature of CNT to less than 500°C leads to the formation of carbon nanowalls on the CNF instead of CNT. This simple fabrication method allows an easy preparation of hierarchical carbon nanostructures over a large surface area, as well as a simple manipulation of such material in order to integrate it into nanodevices.     

软硬混编预制体增强沥青基4D-C/C材料的拉伸破坏行为

以X-Y平面依次铺设炭纤维束、Z向穿插炭棒的4D软硬混编为预制体,采用沥青液相常压、高压浸渍/炭化-石墨化循环致密工艺制备4D-C/C复合材料。通过该材料Z向(炭棒方向)的拉伸实验,测定其拉伸性能和力学行为,并采用SEM分析试样表面及断口形貌。结果表明:宏观上拉伸试样以炭棒整体拔出的形式破坏;细观尺度上,试样表面形成了与载荷方向垂直的贯穿性裂纹,裂纹以2 mm左右的距离呈等间距分布;材料进一步的破坏过程中,基体裂纹在X-Y向纤维束中呈线性扩展,快速分割了基体材料,使4D-C/C复合材料的拉伸破坏演变为1D-C/C复合材料的破坏模式,由于炭棒与基体炭界面结合弱,炭棒以拔出方式失效和破坏。     

Diamond formation on carbon/carbon composite

A carbon/carbon composite was used as substrate for low-pressure diamond deposition. To enhanced diamond nucleation on carbon/carbon composites, a total of ten surface preparation methods have been investigated. These methods involved the use of atomic hydrogen etching, mechanical polishing, sonication, or coating. Diamond nucleation was found to occur on either the defects of the carbon/carbon composite substrates or diamond particulate left on the substrates. The defects were created primarily by atomic hydrogen etching during the coating process. Seeding with diamond powders was performed by dip coating, sonication, or spray-coating processes. It was found that these seeding processes resulted in excellent nucleation of diamond.     

Graphitization behaviour of carbon fibre-glassy carbon composites

Carbon fibre-carbon composites were fabricated by aligning PAN-based carbon fibre unidirectionally in furfuryl alcohol resin char. The graphitization behaviour was investigated by an X-ray diffraction technique and by the measurement of magnetoresistance. The time-temperature superimposition study for interlayer spacing resulted in an activation energy of 242±35 kcal mol⁻¹. The kinetic study on magnetoresistance agreed with the result of X-ray measurement. The activation energy is that for the graphitization of the layer structure formed in the glassy carbon matrix of the composites. The graphitization mechanism of the layer structure is the same as that of soft carbons.     

Mesoscale evolution of non-graphitizing pyrolytic carbon in aligned carbon nanotube carbon matrix nanocomposites

Polymer-derived pyrolytic carbons (PyCs) are highly desirable building blocks for high-strength low-density ceramic meta-materials, and reinforcement with nanofibers is of interest to address brittleness and tailor multi-functional properties. The properties of carbon nanotubes (CNTs) make them leading candidates for nanocomposite reinforcement, but how CNT confinement influences the structural evolution of the PyC matrix is unknown. Here, the influence of aligned CNT proximity interactions on nano- and mesoscale structural evolution of phenol-formaldehyde-derived PyCs is established as a function of pyrolysis temperature (\(T_{\mathrm {p}}\)) using X-ray diffraction, Raman spectroscopy, and Fourier transform infrared spectroscopy. Aligned CNT PyC matrix nanocomposites are found to evolve faster at the mesoscale by plateauing in crystallite size at \(T_{\mathrm {p}}\) \(\sim\)800 \(^{\circ }\hbox {C}\), which is more than \(200\,\,^{\circ }\hbox {C}\) below that of unconfined PyCs. Since the aligned CNTs used here exhibit \(\sim\)80 nm average separations and \(\sim\)8 nm diameters, confinement effects are surprisingly not found to influence PyC structure on the atomic-scale at \(T_{\mathrm {p}}\) \(\le \)1400 \(^{\circ }\hbox {C}\). Since CNT confinement could lead to anisotropic crystallite growth in PyCs synthesized below \(\sim\)1000 \(^{\circ }\hbox {C}\), and recent modeling indicates that more slender crystallites increase PyC hardness, these results inform fabrication of PyC-based meta-materials with unrivaled specific mechanical properties.     

Development of vapor grown carbon fibers (VGCF) reinforced carbon/carbon composites

C/C composites are developed using vapor grown carbon fibers (VGCF) with two types of pitches as matrix precursor. The composites are carbonized at 1000°C by applying the isostatic pressure throughout the carbonization process and further heat treated at different temperatures up to 2500°C in the inert atmosphere. By applying iso-static pressure one can able to developed VGCF based C/C composites possessing the very high bulk density (1.80 g/cm³) and apparent density (2.01 g/cm³) only by heat treatment up to 2500°C without any densification cycle. This high value of density is due to the extremely strong fiber-matrix interactions and self sintering between the VGCF fibers during carbonization process under iso-static pressure. From the SEM study it reveals that, fiber-matrix interactions are strong and fiber boundaries merges with each other, also there is not a evidence of matrix shrinkage cracks in case 1500°C heat treated composites. On the other hand, in 2500°C heat treated composites, there is evidence of uniform fiber-matrix interfacial cracks and porosity in nanometer dimensions. This is due to the change in fiber morphology above HTT 1500°C. But the formation of nano width cracks does not affect on the mechanical properties of composites. The compressive strength increases from 95MPa of 1500°C to 105 MPa of 2500°C heat treated composites. However, hardness decreases due to the increase in the degree of graphitization of composites on 2500°C. The study reveals that by controlling processing condition and the uniform dispersion of VGCF fibers in the matrix phase, it can be possible to developed nano porosity at fiber-matrix interface.