多层金属复合材料的应变局部化延迟和抗断裂失稳机理

多层金属复合材料在航天航空、汽车、船舶、核能电力领域中起着非常重要的作用。相比于传统单一金属,多层金属复合材料具有超高的塑性变形能力和断裂韧性。综述了多层金属复合材料在塑性变形过程中的应变局域化延迟和抗断裂失稳的特征和机理,归纳出周期性颈缩、脱层断裂、隧道裂纹、弥散剪切带对抑制多层金属复合材料塑性失稳的作用机理,并阐明脱层断裂、裂纹分叉、隧道裂纹对多层金属复合材料的增韧机理,和对韧脆转变行为的作用规律,可为金属材料强韧化提供新的设计思路和技术支撑。     

纳米多层结构实现硬质薄膜韧化的方法、机理与应用

硬质薄膜的韧化正成为气相沉积硬质薄膜研究和应用的重点。纳米多层结构设计是实现硬质薄膜强韧化的有效方法。本文介绍了纳米多层薄膜组元和韧化机理,讨论了周期、调制周期比、微观结构等子层因素对强韧化的影响,以及耐磨损、耐冲蚀场合的应用现状、问题以及原因。微裂纹在多层界面间偏折是纳米多层结构韧化的主要机理,但纳米多层结构界面越多,其裂纹萌生源越多,如果界面韧性较差,纳米多层结构会很快发生层-层剥离而失效。因此,纳米多层薄膜的韧化效果决定于界面的质量,而不是数量。必须获得高质量的层间界面,从断裂力学角度考虑抑制微裂纹的扩展,才能发挥纳米多层结构薄膜的优势。     

高强度热冲压钢板强韧性工艺优化研究

为改善强韧性,本文基于热冲压高强度钢板强度、塑性和韧性指标,选取加热温度、保温时间和开始淬火温度为设计因子,引入Kahn试验获得高强度热冲压硼钢撕裂强度和单位面积裂纹形核功来表征材料断裂韧性,进行多指标综合评分的L9(34)正交试验设计,以研究不同淬火工艺参数对热冲压高强钢强韧性的影响规律.结果表明:在加热温度为920~950℃、保温时间1 min、开始淬火温度为650~700℃条件下,热冲压硼钢SPFH具有优良的成形性能和强韧化指标.采用优化后工艺进行典型车身结构件热冲压试验,其撕裂强度、单位面积裂纹形核功和强韧比分别提升10.91%、20.32%和22.17%,在保证强度的基础上韧性得到了大幅度提高.     

TiC颗粒增韧SiC基复合材料及其冷处理研究

研究了TiC_P粒径与TiC_P/SiC复合材料的抗弯强度和断裂韧性之间的关系,探讨了低温冷处理对复合材料性能的影响.结果表明:添加适宜粒径的TiC颗粒能够提高SiC材料的强度和韧性,但同时提高强度和韧性的粒径范围很窄.对复合材料进行低温冷处理,不仅可以进一步提高强度和韧性,而且可以改变增韧的粒径范围,使增韧和增强的粒径重合范围变宽.因此,形成一个较宽范围的强韧化区,为材料的强韧化设计和工艺的制定提供了依据.      

纳米金属多层膜的强韧化及其尺寸效应

如何有效地协调和平衡材料强度与韧性之间的矛盾,大幅度地提高结构材料的损伤容限,是非均质金属材料微观结构敏感性设计的巨大挑战。纳米金属多层膜作为一类典型的非均质金属材料,由于不仅可以调整其组元几何和微观结构尺度,而且可以引入具有不同本征性能的组元材料和不同结构的层间异质界面,因此在获得高强高韧金属结构材料方面具有潜在的能力。结合当前国内外有关金属多层膜塑性变形强韧化机制及其尺寸与界面效应研究的最新进展,分别阐述了晶体/晶体Cu/X(X=Cr,Nb,Zr)与晶体/非晶Cu/Cu-Zr金属多层膜/微柱微观结构-尺寸约束-服役性能三者之间的关联性,并对纳米金属多层膜研究的发展趋势进行了展望。     

基于DIW的“互锁”型层状钛基复合材料成型及其力学性能

采用浆料直写打印(direct ink writing, DIW)技术对0.8%(体积分数，下同)BNNSs/TC4浆料和TC4浆料进行双材料互嵌打印，构建层间“互锁”界面。结合DIW和快速热压烧结(fast hot pressed sintering, FHPS)技术得到纳米TiB增强的层间“互锁”型致密层状TC4-TiB/TC4复合材料，并对其力学性能进行研究。结果表明：烧结后成功保留了层间“互锁”结构；利用DIW制备的层间“互锁”型层状TC4-TiB/TC4复合材料与未作构型的增强相均匀分布的0.4%TiB/TC4复合材料相比，强度提升了9.1%,达到1206 MPa,但韧性并未下降。分析发现，“互锁”的层间界面使裂纹发生极大的偏转，阻碍裂纹扩展，提升整体材料的韧性，为成型复杂强韧复合材料构件提供了思路。     

重点实验室研究进展

钼合金具有室温脆性以及强度低、延性差等本征特性,导致其深加工困难、产品性能低、应用领域受限。如何同步提高钼合金的强度与延、韧性,一直是本领域的挑战性难题。西安交通大学金属材料强度国家重点实验室孙军教授课题组经过多年努力,揭示了稀土氧化物掺杂钼合金中晶粒及晶内与晶界粒子强韧化尺寸效应特性和机理,建立了强韧化定量解析模型,证实了细化稀土氧化物及钼晶粒均可有效提高钼合金的强度和延、韧性,提出了纳米掺杂强韧化的新思路。并据此开发了分子级掺杂的液相混合制备含纳米稀土氧化物钼合金的关键技术,解决了稀土氧化物的纳米化与非团聚化、及其在钼晶粒内部和晶界均匀弥散分布、纳米超细晶结构的高温稳定性等制约该领域发展的3大“瓶颈”难题。所制备的合金中氧化物平均颗粒尺寸小于80 nm,钼晶粒尺寸可达亚微米级（图1）。这种具有纳米稀土氧化物粒子与超细晶微观结构的钼合金在获得显著强化的同时,其拉伸延性可成倍提高。该新型钼合金的强度与延、韧性均超过已报道的国际一流公司同类材料最好水平（图2）,同时明显降低了其塑脆转变温度,并显著提高了合金高温再结晶温度及高温强度与拉伸延性。     

微观组织结构对C/C复合材料力学行为的影响

采用快速化学液相气化渗透法制备了2D-C/C复合材料,沉积温度为1200-1250℃, 系统压力约0.1MPa.利用偏光显微镜及扫描电子显微镜观察了不同沉积温度制备的基体热解碳的微观组织结构及断口形貌.实验结果表明,1200℃沉积的基体热解碳中粗糙层组织占大多数,其弯曲强度较高、韧性较低; 1250℃的基体热解碳呈现为光学各向异性程度不同的光滑层/粗糙层交替层状组织,其弯曲强度较低、韧性较高,具有非脆性断裂行为.不同微观结构的材料具有不同的强度及断裂模式,除了纤维/基体间界面结合强度不同外,不同温度沉积得到的热解碳微观结构的不同引起裂纹在不同微观结构碳层内的扩展阻力也会不同.此外,裂纹在光滑层/粗糙层界面处的偏转会导致断裂面的高低不平,从而使后者韧性增强.     

利用最小晶格错配和强有序效应发展超强金属材料（英文）

本文概括总结了传统超高强度钢的强韧化机制,针对2 GPa以上超高强度钢强韧性匹配不足、成本昂贵等突出问题,提出了最小化晶格错配和强有序效应以发展新型超强金属材料,并协同利用高密度共格粒子、高密度位错、弹性畸变中心等多重效应,克服传统共格析出强化合金低塑韧性问题,实现超高强度钢良好强韧性匹配.     

通孔构型Ti6Al4V/Ti2AlC-TiAl基叠层复合板材的组织和性能

将Ti-Al-TiC混合粉末和通孔构型TC4钛合金箔(Ti6Al4V)依次叠放装入模具,采用放电等离子烧结技术( SPS)制备了珍珠层结构Ti6Al4V/Ti2 AlC-TiAl基叠层复合板材.采用XRD、SEM、EBSD等测试手段分析相组成及微观结构,测试其室温力学性能,研究其强韧化及断裂机理.结果表明,Ti2 AlC理论生成量为10% (质量分数)时,复合板材在垂直于叠层方向弯曲强度和断裂韧性达到最大值,分别为645. 77 MPa和25. 06 MPa· m1/2 .通孔构型TC4钛合金强韧层设计改变了裂纹扩展路径,使裂纹扩展驱动力不断被削弱,同时第二相Ti2 AlC对裂纹扩展也产生阻碍作用,从而提高了TiAl基叠层复合板材的综合力学性能.     

Introducing a hierarchical structure for fabrication of a high performance steel

The multifunctional diversities existing in nature provide clues to speculate the structure–property–function relationships. A hierarchically structured steel is designed by using principles derived from nature and fabricated in situ by a one-step method of surface mechanical attrition treatment (SMAT). The microstructure of the processed steel is characterized by multilayered structure with hard nanocrystalline surface and compliant inner-layer, in particular with a smooth mechanical gradient induced by dual-phase constituents and multiscale grain size distribution. The hierarchically structured steel exhibits simultaneously high stiff, strong and large ductility, which originate from the joint deformation mechanisms of distinct reinforcing layers. The four layers present their own unique deformation mechanisms, including second-phase hardening, transformation induced plasticity and twin strengthening. The unique spatial form of gradation can release stress concentration and improve energy-dissipation leading to exceptional mechanical properties compared with the uniform materials.     

Dynamic crack initiation toughness of 4340 steel at constant loading rates

Determination of fracture toughness for metals under quasi-static loading conditions can follow well-established procedures and ASTM standards. The use of metallic materials in impact related applications requires the determination of dynamic crack initiation toughness for these materials. There are two main challenges in experiment design that must be overcome before valid dynamic data can be obtained. Dynamic equilibrium over the entire specimen needs to be approximately achieved to relate the crack tip loading state to the far-field loading conditions, and the loading rate at the crack tip should be maintained near constant during an experiment to delineate rate effects on the values of dynamic crack initiation toughness. A recently developed experimental technique for determining dynamic crack initiation toughness of brittle materials has been adapted to measure the dynamic crack initiation toughness of high-strength steel alloys. A Kolsky pressure bar is used to apply the dynamic loading. A pulse shaper is used to achieve constant loading rate at the crack tip and dynamic equilibrium across the specimen. A four-point bending configuration is used at the gage section of the setup. Results are presented which show a monotonically increasing rate dependence of crack initiation toughness for 4340 high-strength steel.     

Enhancing the mechanical properties of low-carbon steel by a graded dislocation microstructure

In the present paper, the microstructures and mechanical properties of a low-carbon steel processed by graded pre-torsion (PTO) and homogeneous pre-tension (PTE), respectively, have been investigated. Experimental results demonstrate that both PTO and PTE can improve the strength of the low-carbon steel, but at a loss of ductility and toughness. However, a much better strength–ductility–toughness synergy is achieved in samples processed by graded PTO than that in samples subjected to PTE. This enhancement of comprehensive mechanical properties is due to the formation of a graded microstructure, that is, the dislocation-density increases gradually with decreasing the depth from the sample surface. This study provides a strategy for enhancing the mechanical properties of metallic materials by graded plastic deformation.     

高强韧金属材料中微结构的研究和应用

金属结构材料中的共格界面强化近年来受到广泛关注,虽然,该方法被证明是一种可同时实现强度、韧性双增的有效途径,但该类材料的制备往往受到尺寸、设备或工艺的制约.近期,一种全新的原位纳米颗粒强化技术被提出,旨在通过弥散分布的共格纳米粒子实现材料微观组织的优化及综合性能的提升.文中以铁基合金、铜合金、铝合金为例,对原位纳米颗粒...     

高强度超细晶金属材料塑性行为及增塑研究进展

强度和塑性是金属结构材料最重要的力学性能指标,金属高性能化的关键是在高强度水平下保证良好的塑性,然而两者往往不能兼顾。在众多强化方法中,晶粒细化长期以来被认为是强化金属最理想的手段,在传统晶粒尺寸范围,细化晶粒既可以显著提高材料的强度,又能改善材料的塑韧性。因此,近几十年来超细晶/纳米晶金属得到了广泛研究和发展,出现了以大塑性变形(SPD)、先进形变热处理(ATMP)技术为代表的超细晶制备方法,所得晶粒可以细化到亚微米或纳米尺度,金属性能大大提高。然而,大量研究证实当晶粒细化到亚微米或纳米尺度时金属强度提高但塑性显著下降,与传统的细晶强化规律不符。对此,国内外学者进行了很多研究,试图阐明其机理、揭示晶粒超细化导致塑性降低的物理本质。此外,由于细化晶粒方法受到塑性的限制,新的高强度水平下增强塑性的方法成为钢铁材料高性能化的研究热点。针对塑性下降的事实,为了进一步提高超细晶金属材料性能,研究者开展了许多增强塑性的工作,获得了较好的效果,但仍存在一些不足。关于金属晶粒超细化导致塑性降低的普遍共性现象,目前广泛认可的理论主要有晶界捕获(吸收)位错的动态回复理论、位错运动湮灭理论、高初始位错密度以及位错源缺失机制等。前三者都主要关注超细晶金属材料低(无)加工硬化能力,并将其归结为延伸率降低所致。主要是因为低(无)加工硬化使材料在变形早期发生塑性失稳或局部变形从而表现出低塑性。超细晶金属增塑研究主要体现在增塑方法和机理方面,目前,增塑方法主要有(1)形成纳米孪晶;(2)获得粗晶-细晶双峰组织;(3)利用相变诱发塑性/孪生诱发塑性(TRIP/TWIP)效应;(4)引入铁素体软相;(5)利用纳米第二相粒子等。这些增塑方法的主要机理是利用组织结构的改变提高超细晶金属的加工硬化能力以维持良好的均匀塑性变形以及利用组织相变提高塑性。本文归纳了常用的超细晶金属制备方法,综述了超细晶金属材料塑性降低的研究进展,总结了超细晶金属增塑的研究结果,分析了目前研究中存在的不足,探讨了超细晶金属增强增塑的发展趋势,以期为超细晶金属塑性降低理论及增强增塑研究提供参考。     

Effect of multi-directional forging and ageing on fracture toughness of Al–Zn–Mg–Cu alloys

Strength, ductility and fracture toughness are the most important mechanical properties of engineering materials. In this work, an Al–Zn–Mg–Cu alloy was subjected to multi-directional forging (MF) and ageing treatment. Microstructural evolution was studied by optical and electron microscopy and strength, ductility and fracture toughness were researched. After MF, the dislocation density was increased and the microstructure was refined. The strength and fracture toughness were increased, while the ductility was decreased sharply. Without compromising the strength, the ductility was improved significantly after ageing. The fracture toughness was increased further. The coarse and discontinuously distributed grain boundary precipitates were found to be responsible for higher fracture toughness of the fine-grained structure Al–Zn–Mg–Cu alloy.     

Fatigue crack growth rates and fracture toughness in electroslag refined En 52 steel

En 52 steel has been electroslag refined and the resultant effects of refining on its mechanical properties have been assessed. It was found that refining caused a decrease in fatigue crack growth rates and increases in fatigue strength, fracture toughness, Charpy fracture energy and tensile ductility. Fatigue crack growth rates in region I and in region III were found to be considerably lower in the electroslag refined steel: they were unaffected in region II. The fracture toughness values for the electroslag refined steel are nearly twice those estimated for the unrefined steel. Measurements on heat-treated samples have shown that the electroslag refined steel has a better response to heat-treatment. The improvement in the mechanical properties is explained in terms of the removal of nonmetallic inclusions and a reduction in the sulphur content of the steel.     

Multi-length scale micromorphic process zone model

The prediction of fracture toughness for hierarchical materials remains a challenging research issue because it involves different physical phenomena at multiple length scales. In this work, we propose a multiscale process zone model based on linear elastic fracture mechanics and a multiscale micromorphic theory. By computing the stress intensity factor in a K-dominant region while maintaining the mechanism of failure in the process zone, this model allows the evaluation of the fracture toughness of hierarchical materials as a function of their microstructural properties. After introducing a multi-length scale finite element formulation, an application is presented for high strength alloys, whose microstructure typically contains two populations of particles at different length scales. For this material, the design parameters comprise of the strength of the matrix–particle interface, the particle volume fraction and the strain-hardening of the matrix. Using the proposed framework, trends in the fracture toughness are computed as a function of design parameters, showing potential applications in computational materials design.     

Alloy design by dislocation engineering

Ultra-high strength alloys with good ductility are ideal materials for lightweight structural application in various industries. However, improving the strength of alloys frequently results in a reduction in ductility, which is known as the strength-ductility trade-off in metallic materials. Current alloy design strategies for improving the ductility of ultra-high strength alloys mainly focus on the selection of alloy composition (atomic length scale) or manipulating ultra-fine and nano-grained microstructure (grain length scale). The intermediate length scale between atomic and grain scales is the dislocation length scale. A new alloy design concept based on such dislocation length scale, namely dislocation engineering, is illustrated in the present work. This dislocation engineering concept has been successfully substantiated by the design and fabrication of a deformed and partitioned (D&P) steel with a yield strength of 2.2 GPa and an uniform elongation of 16%. In this D&P steel, high dislocation density can not only increase strength but also improve ductility. High dislocation density is mainly responsible for the improved yield strength through dislocation forest hardening, whilst the improved ductility is achieved by the glide of intensive mobile dislocations and well-controlled transformation-induced plasticity (TRIP) effect, both of which are governed by the high dislocation density resulting from warm rolling and martensitic transformation during cold rolling. In addition, the present work proposes for the first time to apply such dislocation engineering concept to the quenching and partitioning (Q&P) steel by incorporating a warm rolling process prior to the quenching step, with an aim to improve simultaneously the strength and ductility of the Q&P steel. It is believed that dislocation engineering provides a new promising alloy design strategy for producing novel strong and ductile alloys.