钢铁件涂装前铁系磷化工艺研究

通过正交试验优选出一种新的常温铁系磷化工艺:氧化锌0.5g/L,磷酸5mL/L,酒石酸0.5g/L,马日夫盐0.5g/L,氟钛酸5.0g/L,氟锆酸1.5g/L,铬明矾5.0g/L,硫脲2.0g/L,钼酸钠0.75g/L,成膜时间6.0min。该磷化液游离酸度为3,总酸度为17。经此磷化液磷化后的冷轧钢铁试片表面磷化膜的致密性和耐腐蚀性与普通铁系磷化相比均有提高,耐硫酸铜点滴时间达50s,后续漆膜的附着力为0级,冲击强度为50kg·cm。该磷化液不含亚硝酸钠,可常温处理,沉渣少,成本低,可与各种涂装工艺配合使用。     

粉末涂装过程中的缺陷分析及对策IV.附着力（Ⅱ）

3.3.2表面调整表面调整的作用是在基材上形成很多晶点,细化磷化膜结晶。如果表面调整失效,钢铁锌系磷化膜呈蓝彩色,膜粗糙,与基材的结合力不佳,最终导致涂层的附着力也不合格 铝及铝合金的锌系磷化膜异常粗糙,结晶颗粒大,膜与基材的结合力差,最终导致涂层的附着力也不合格 锌及锌合金基本无磷化膜,表面容易挂灰,涂层的附着力也不合格。     

光整热镀锌板磷化过程中铝离子的影响及消除

将光整热镀锌板磷化技术用于空调器的生产，探讨了磷化液中铝离子对磷化膜质量的影响，在磷化液中加入氟化钠可消除铝离子的影响，介绍了铝离子的分析方法，该工艺所得磷化膜结晶细致，与涂层附着力好。     

机床零件磷化常见的问题及改进措施

1机床零件磷化常见缺陷及防止方法 1．1磷化膜结晶粗糙多孔产生原因：磷化槽液中游离酸度过高,磷化液中氧化剂量不足,槽液中亚铁离子含量过高,零件表面有残酸,发生过腐蚀。防止方法：降低槽液中游离酸的含量,增加氧化剂比例,加双氧水进行调整,加强中和及水洗,控制酸洗浓度和时间。     

钢骨架表面磷化处理的研究

探讨磷化条件对钢骨架表面磷化膜形态及钢-NR粘合性能的影响。结果表明，采用锌钙系磷化液处理钢骨架的优化条件为：总酸点35，游离酸点5，磷化温度60℃，磷化时间6min。采用该条件处理的钢骨架磷化膜致密、厚度适中、厚薄较均匀、表面略粗糙，钢-NR粘合性能达到或超过采用抛丸法处理的钢-NR粘合性能。     

铝表面常温锌系磷化工艺的研究及应用

使用自制磷化液在工业喷淋线上实现了铝材表面的锌系磷化,利用扫描电镜、能谱仪及X-射线衍射仪研究了磷化膜的表面形貌和晶体结构,研究结果表明,所得磷化膜均匀、致密、表面光滑。喷淋生产线制备的磷化膜的ρs为1.9～2.5g/m2,δ膜为1.9～2.3μm。     

环保型单组分低温磷化液的研制和应用

从环保、质量和处理工艺的角度,阐述了环保型单组分彩膜和灰膜磷化液的配方和制备工艺,并列举了该丙种磷化液的性能测试结果。讨论了磷化槽液的维护与调整,以及磷化促进剂的选择。     

涂装前处理冷轧板磷化膜白点缺陷研究

研究一次涂装前处理冷轧板上的磷化膜“白点”缺陷,通过对工序进行排查、设计验证试验,应用扫描电镜、扫描电镜能谱仪等对“白点”问题进行分析。研究发现：冷轧板上的磷化膜“白点”部位几乎无磷化膜附着,金属光泽的基材与周围银灰色的磷化膜形成颜色反差,表现为“白点”。其根本原因是由于车身经过水洗后冷轧板表面发生锈蚀,附着在板材表面的氧化铁在磷化槽内先被酸解,延迟了磷化反应上膜时间,导致锈蚀区几乎无磷化膜覆盖。通过对预水洗添加一定量的脱脂剂,成功解决了车身冷轧板上的磷化膜“白点”缺陷。     

清洁型低温低磷磷化工艺

介绍了一种环境友好的磷化工艺,其主要特点有:成本低(原液与工作液体积比为1∶100),沉渣少,液温低(25~35°C),喷淋成膜速度快(2.0~5.0 min),膜厚0.8~1.0μm。该工艺既适用于黑色钢铁件,也适用于锌、铝及其合金件,维护十方简便(不需要测量和控制磷化液游离酸度)。因工作液含磷量仅1.2 mg/L,故可不经处理直接排放废水。所得磷化膜致密,可作为防护装饰性涂层的底层。详细介绍了该工艺的流程及操作规范,并给出了其在热水器上盖磷化中的应用实例。     

单组份环保型中温锌钙系磷化液的研究

给出了磷化液的最佳配方，通过硫酸铜点滴法及失重法对磷化膜进行评定。讨论了空气湿度，磷化时间对磷化膜层耐蚀性的影响及磷化时间与膜重的关系。试验中发现含添加剂A、B的磷化液较只含添加剂A的磷化液得到的磷化膜的耐蚀性约提高2-5倍，磷化膜结晶均匀，致密，深灰色，耐蚀性较为理想，并与空气的相对湿度有明显的线性关系。随磷化工艺的不同得到的膜重在5-15g/m^2之间，磷化液为单组份，具有易于操作，无需进行表面调整，节省工作时间，环保性能好等优点，适用于大批量钢铁工件的磷化生产。     

Peel Adhesion of Solid Films-The Surface and Bulk Effects

The peel strength of rubber and paint films has been measured over a range of peeling velocities using a dead weight method. At low peel rates the peel force is fairly constant but rises rapidly at higher peeling speeds.

Experiments show that the peel strength is a function both of the energy of interfacial bonds which must be broken as peeling proceeds and of bulk energy losses in a viscoelastic peeling material.

The interfacial effect has two components: an equilibrium surface force which accounts for the peel strength at low velocities, and a viscous peeling force which depends on the peeling rate. This viscous interfacial force explains the increase in peel strength of purely elastic films at higher peeling velocities.

The energy loss in the bulk of the peeling film introduces two additional effects: a magnification of the peel strength in steady peeling over a certain velocity range, and a slowing down or stopping of peeling as transient relaxation occurs shortly after the application of the peel force.     

Relationship between Viscoelastic and Peeling Properties of Model Adhesives. Part 1. Cohesive Fracture

The viscoelastic and peeling properties of polybutadiene/tackifying resin compatible blends have been studied in detail. Viscoelastic properties have been described through the variations of the complex shear modulus, G*(ω), as a function of frequency, ω and peeling properties through the variations of peeling force (F) as a function of peeling rate (V).

After showing the objective character of the peeling curves obtained, the variations of the peeling force and peeling geometry have been studied as a function of volume fraction of the tackifying resin.

In this first paper, the analysis is focused on the first domain of the peeling curves, i.e. the cohesive fracture region. In this region, the peeling properties have been related to the viscoelastic properties in the terminal region of relaxation. It is shown that the longest relaxation time, τ_o, is a reducing parameter of the peeling curves, so a peeling master curve-which is independent of temperature, resin volume fraction and polymer molecular weight-may be defined. Furthermore, the variations of the test geometry as a function of peeling rate have been investigated: the variations of the radius of curvature of the aluminium foil have been analyzed with respect to the viscoelastic behavior of the adhesive, which in fact governs the test geometry.

A detailed analysis of all these features leads to a model which allows one to calculate the peeling curves in the cohesive domain from the adhesive formulation.     

Peel Adhesion of Solid Films-The Surface and Bulk Effects

The peel strength of rubber and paint films has been measured over a range of peeling velocities using a dead weight method. At low peel rates the peel force is fairly constant but rises rapidly at higher peeling speeds.

Experiments show that the peel strength is a function both of the energy of interfacial bonds which must be broken as peeling proceeds and of bulk energy losses in a viscoelastic peeling material.

The interfacial effect has two components: an equilibrium surface force which accounts for the peel strength at low velocities, and a viscous peeling force which depends on the peeling rate. This viscous interfacial force explains the increase in peel strength of purely elastic films at higher peeling velocities.

The energy loss in the bulk of the peeling film introduces two additional effects: a magnification of the peel strength in steady peeling over a certain velocity range, and a slowing down or stopping of peeling as transient relaxation occurs shortly after the application of the peel force.     

Operating window for the peeling of polyimide film

The peeling behavior of polyimide film coated on steel substrates was experimentally investigated and compared with existing models. An operating window for peeling, which is defined as a closed domain for steady and defect‐free peeling, is presented in terms of peeling force versus residual solvent content. The window is bounded by two major defects: the film becomes too brittle for peeling at high peeling force, and stick‐slip striation defect appears at low peeling force. There exists a critical residual solvent content below which the adhesion between the polyimide film and the substrate is too strong and then peeling is impossible. Existing models for predicting steady peeling and the onset of peeling defects have been modified and applied to setup the boundaries of the operating window. There also exists another operating window for drying of polyimide and is presented in the form of drying temperature versus film thickness. POLYM. ENG. SCI., 2010. © 2009 Society of Plastics Engineers     

Relationship between Viscoelastic and Peeling Properties of Model Adhesives. Part 1. Cohesive Fracture

The viscoelastic and peeling properties of polybutadiene/tackifying resin compatible blends have been studied in detail. Viscoelastic properties have been described through the variations of the complex shear modulus, G*(ω), as a function of frequency, ω and peeling properties through the variations of peeling force (F) as a function of peeling rate (V).

After showing the objective character of the peeling curves obtained, the variations of the peeling force and peeling geometry have been studied as a function of volume fraction of the tackifying resin.

In this first paper, the analysis is focused on the first domain of the peeling curves, i.e. the cohesive fracture region. In this region, the peeling properties have been related to the viscoelastic properties in the terminal region of relaxation. It is shown that the longest relaxation time, τ_o, is a reducing parameter of the peeling curves, so a peeling master curve-which is independent of temperature, resin volume fraction and polymer molecular weight-may be defined. Furthermore, the variations of the test geometry as a function of peeling rate have been investigated: the variations of the radius of curvature of the aluminium foil have been analyzed with respect to the viscoelastic behavior of the adhesive, which in fact governs the test geometry.

A detailed analysis of all these features leads to a model which allows one to calculate the peeling curves in the cohesive domain from the adhesive formulation.     

钢丝帘布的剥离测试方法研究

针对钢丝帘布剥离测试结果的系统性不稳定情况,研究剥离力测试结果的影响因素。结果表明:利用夹持端包布提高夹持摩擦力不能改善剥离测试效果,反而导致试样水平端面硫化压力分布不均造成剥离力下降;帘布间敷贴带束胶片虽然能大幅提高剥离力,但从剥离后覆胶状态来看更多反映的是帘布间胶料的撕裂强度;剥离拉伸速率越大,胶料破坏方向越平直,剥离力有下降趋势;硫化时间太长导致的硫化返原可明显降低剥离力。     

水果去皮剂的研制

研制了适用于苹果、梨、桃、李等水果的去皮剂,它由表面活性剂及助剂组成（质量比１∶０．５）,表面活性剂选取分子碳数为１２的月桂酸及司盘－２０（质量比１∶０．５）,助剂由柠檬酸、碳酸钠、氯化钠组成（质量比２∶２∶１）。在苹果去皮时,使用去皮剂及氢氧化钠的质量分数分别为０．５％和６％的水溶液,６０℃浸泡５～６ｍｉｎ,去皮率达到１００％。     

The Shapes of Peeling Solid Films

A theory is developed to describe the shape of a long thin elastic film peeling from a rigid substrate under a constant load. The theory is verified by static measurements of spring steel strip and by slow peeling experiments using rubber and paint films. Extension of the theory to the case of viscoelastic peeling films demonstrates how the film shape in such a system depends on peeling velocity. Reasonable agreement with experiment is obtained.     

固化工艺参数对胶粘剂180°剥离强度的影响

以自制胶粘剂为基础,研究了剥离强度测试用样条的制备工艺对180°剥离强度的影响。结果表明:样条制备时的温度、压力、时间、胶层厚度和被粘材料表面粗糙度等因素对剥离强度影响较大,并且有一定的规律性,说明对每种胶粘剂的剥离强度测试,除统一测试标准外,还需研究测试用样条的适宜制备工艺,以降低剥离强度的测试误差。     

Relationship Between Viscoelastic and Peeling Properties of Model Adhesives. Part 2. The Interfacial Fracture Domains

The viscoelastic and peeling properties of polybutadiene/tackifying resin compatible blends have been studied in detail. Viscoelastic properties have been described through the variations of the complex shear modulus, G*(w), as a function of frequency, W, and peeling properties through the variations of peeling force (F) as a function of peeling rate (V).

The first paper of this series presented the cohesive fracture domain and the present paper explores the interfacial fracture domain: (i) rubbery interfacial (interfacial 1); (ii) stick-slip; (iii) glassy interfacial (interfacial 2). After a general survey of the properties in the three domains we present a quantitative relationship between the peeling and linear viscoelastic properties as a function of the adhesive formulation, discussing the use of time-temperature equivalence for adhesive properties. The third part of the paper presents the trumpet model of de Gennes describing the crack shape and propagation: starting from a mechanical analysis of the peeling test, it is shown how one may calculate the variations of the peeling force as a function of peeling rate in the various interfacial fracture domains: this model defines a single interfacial fracture criterion which coexists with the cohesive fracture criterion defined earlier, whatever the fracture location.

We present as a conclusion a critical discussion of the relevance and physical meaning of such a criterion and present a new outlook for the modeling and improvement of adhesive formulations.