CN113165337B - 基于钒合金和钢的复合材料的制造方法 - Google Patents

基于钒合金和钢的复合材料的制造方法 Download PDF

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CN113165337B
CN113165337B CN201980081325.8A CN201980081325A CN113165337B CN 113165337 B CN113165337 B CN 113165337B CN 201980081325 A CN201980081325 A CN 201980081325A CN 113165337 B CN113165337 B CN 113165337B
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composite
composite material
steel
vanadium alloy
thickness
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CN113165337A (zh
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谢尔盖·阿纳托尔叶维奇·尼库林
安德烈·鲍里索维奇·罗日诺夫
斯坦尼斯拉夫·奥列戈维奇·罗加乔夫
弗拉季斯拉夫·阿列克谢维奇·贝洛夫
塔季扬娜·阿纳托尔耶芙娜·涅恰金娜
弗拉基米尔·马尔科维奇·哈特克维奇
亚历山德拉·帕夫洛芙娜·巴拉诺娃
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SCIENCE AND TECHNOLOGY MISIS, National University of
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Abstract

本发明涉及复合材料的生产，即基于金属和合金的复合材料的变形热处理。一种由钒合金内层V‑3‑11wt％Ti‑3‑6wt％Cr和铬含量不低于13wt％的铁素体级不锈钢的两个外层组成的复合材料的生产方法，包括制备由所述内层和外层组成的复合工件，加压热处理，随后暴露在炉中。所制备的复合工件，其内层的厚度比不锈钢外层的总厚度大1.5‑2倍，在所述工件的压力下，在1,050‑1,150℃的温度范围内以还原30‑40％进行热加工，随后暴露1‑3小时，降温至500‑700℃，然后通过加热至850‑950℃对工件进行退火，保持2‑4小时，随后在炉中冷却。生产模式提供了钒合金和尺寸为60‑70μm的增加厚度的钢之间的扩散连接区域的形成，这在初始复合坯料中的给定厚度比下导致产生更复杂机械性能的复合材料。

Description

基于钒合金和钢的复合材料的制造方法
技术领域
本发明涉及复合材料的工业技术，更具体地，涉及基于金属和合金的复合材料的变形和热处理，并且可以用于制造半成品和基于它们的片材、带材、管材和棒材形式的产品，其在高温下具有优异的机械、腐蚀和辐射性能。
现有技术
已知的是使用各种压力处理技术(锻造、轧制、压制等)以及中间和最终热处理(退火、正火等)对金属和合金进行变形和热处理的方法，现有技术提供了半成品和最终产品的所需性能水平，条件是这些半成品和最终产品由均匀的材料制成，但并不总是适用于由复合材料制成的半成品和最终产品，所述复合材料的组分本质上是显著不同的(例如，基于它们的不同金属和合金)并且具有不同物理和机械性能。在这些情况下，以相同技术和工艺设备的适用性为准，至少需要选择特殊的加工模式，以提供在塑性共变形期间材料的均匀变形和复合材料的组分之间的所需扩散结合水平，以及一组最佳物理和机械性能的最终复合材料。
已知的是通过塑性共变形制造复合材料的方法，其中将不同性质的材料的组分放置在袋(或复合模具)中，同时暴露于变形，然后进行热处理，并且最终粘合以产生整个复合材料。在RU 2302044“带铅冷却剂的快中子反应堆燃料棒”中证明了使用这种类型的技术由基于不同金属和合金(钢等)的复合材料制造核反应堆堆芯的关键部件，例如核反应堆燃料棒包壳。该方法的缺点是组分中潜在的变形不均匀性，导致被粘合的组分的厚度不同，因此粘合力不足。组分层中的变形不均匀性取决于组分金属的强度比、组分层的厚度比、变形部位的参数、外部和层间摩擦系数以及复合材料坯料的层的相互布置。变形不均匀性可能导致组分粘合界面处的撕裂。
还已知一种基于钒合金和不锈钢制造片材或管材形式的复合材料的方法，其包括通过在1100℃下组合热轧或压制复合材料坯料并在850℃至1000℃范围内的温度下退火两小时来使用塑性共变形(S.A.Nikulin，S.N.Votinov，A.B.Rozhnov，核电工业用钒合金，莫斯科，莫斯科国立钢铁合金学院，2013，184p.)。根据该方法的层状金属复合材料的制造涉及形成所谓的扩散过渡区，该扩散过渡区表征组分通过接触界面到两侧的转移。扩散过渡区的厚度取决于制造过程的参数(变形量和变形率、温度)和被粘合的材料的参数，但是通常在第一次粘合之后，扩散过渡区的厚度在5-10μm内。扩散过渡区在很大程度上决定了复合材料组分的粘合力和进一步的压力处理阶段而不形成缺陷的可能性。为了根据上述方法由钒合金和钢制造复合材料，在轧制(压制)期间形成的扩散过渡区的厚度在8-10μm内，而在1000℃退火使扩散过渡区加宽60-80μm。在所描述的情况下，扩散过渡区域的厚度在组分之间提供一定程度的粘合，但是不足以在钒合金和钢之间提供可靠且牢固的粘合；这与粘合界面处的组分的非最佳晶粒结构以及由于制造件横截面中的变形不均匀性而导致的在其长度上的不均匀扩散过渡区厚度相结合，并且导致无法提供制造件中的一组所需的机械性能的复合材料。因此，扩散过渡区的厚度不足和组分粘合界面处的非最佳微结构是上述方法的缺点。
选择作为其原型的本文公开的本发明的最接近的对应物是(S.A.Nikulin等人，退火对三层钢/钒合金/钢材料的结构和机械性能的影响，有色金属，2018，No.2，p 70-75)中描述的方法。在该方法中，通过在T＝1100℃下塑性共变形(共挤出)，然后在800-900℃下退火2h来制造基于钒合金和钢的复合材料。该方法提供了相对高的强度和塑性，这是由于形成了稍厚的粘合扩散过渡区(10-30μm)，在复合材料组分粘合界面处没有第二相沉淀，并且在与钒合金的界面处在钢结构中形成了中等尺寸的晶粒(45-70μm)。
该方法的缺点是钒合金和钢之间的扩散过渡区的厚度仍然不足(这可以特别地表示在层具有不同厚度的区域中)，并且所得结构在复合材料横截面上不足够均匀，这可能导致局部剥离和在进一步的压力处理阶段在复合材料层之间形成不连续性。此外，该方法是高功率消耗的，因为它包括当制造的零件在热压处理之后完全冷却时用于随后的退火的再加热。
因此，本发明的一个目的是增加复合材料(钒合金和钢)的组分之间的粘合的扩散过渡区域的厚度，并且避免第二相在粘合界面处沉淀，同时保持钒合金和钢在界面附近的可接受的晶粒尺寸(以及复合材料横截面上的结构均匀性)，以便相对于进一步的复合材料处理阶段提供一组最佳机械性能的材料。本发明的又一个目的是降低该方法的功耗(在变形和热处理阶段)。
本发明的技术结果是复合材料(钒合金和钢)的组分之间的高粘合强度(变形时的试样剥离直到样品失效才发生)，以及高塑性(相对伸长率16％-20％)，在进一步处理阶段在组分粘合界面处不存在剥离，以及该方法的较低功耗。
发明内容
本文公开的制造基于钒合金(钒/钛/铬体系)和不锈钢(选自铁素体钢)的复合材料的方法包括在1050-1150℃范围内的温度下在保护气氛中以还原30-40％进行热压处理复合材料坯料，然后在炉中回火，其作为逐步过程实施，即包括从热处理温度冷却至500-700℃，回火1-3小时，加热至850-850℃，回火2-4小时并在炉中冷却，使得炉中回火的总时间达到3-7小时。
本文公开的方法提供了在钒合金和钢之间形成具有60-70μm的大厚度的扩散粘合区域，其中钒合金和钢的晶粒尺寸的不显著增加、残余应力的减小和无第二相沉淀，这对于复合材料坯料中的层厚度的预设比率提供了一组改善的机械性能的复合材料。本文公开的方法的一个重要方面是总热处理(退火)时间的增加提供了粘合的扩散过渡区的厚度的增加、更均匀的结构和由于再结晶过程导致的材料横截面上的残余应力的减少，同时避免了复合材料组分的晶粒尺寸的预期显著增加和在粘合界面处的第二相沉淀(由于逐步回火顺序的实施)，并因此提供了一组改善的机械性能的材料。此外，本文公开的方法由于在退火之前逐步取消额外的再加热而提供了较低的功耗。
在热处理的实践中，将热处理后的回火时间增加到几小时是可接受的，除非它引起不期望的后果，例如在粘合界面处形成脆性化合物或复合材料的组分中晶粒尺寸的突然生长。使用略低的回火温度(500-700℃)稍微减慢了复合材料中的结构演变过程，但是发展了扩散过程的有利条件，这增加了组分之间的扩散过渡区的厚度并增加了粘合的强度。
本文公开的方法实现如下。使用已知的常规方法制备片材、带材、管材或棒材形式的复合材料坯料，其包括钒合金(V-3-11wt％Ti-3-6wt％Cr)内层和两个不锈钢外层(选自铬含量至少为13wt％的铁素体钢)。该复合材料坯料中钒合金层的厚度比钢层的总厚度大1.5-2.0倍。在1050-1150℃范围内的温度下在保护气氛中以还原30-40％进行热压或热轧复合材料坯料。然后将压制的坯料在保护气氛中在1-3小时内冷却至500-700℃范围内的温度，然后加热至850-950℃，在保护气氛中回火(退火)2-4小时，最后在炉中冷却。
实施例
为了实现本文公开的方法的实施例之一，我们通过示例的方式使用厚度为1850μm的V-4％Ti-4％Cr合金的三层片材坯料，其位于两层08Cr17Ti不锈钢之间，这两层08Cr17Ti不锈钢位于钒合金层的底部下和顶部上，并且具有300μm的总厚度。以包括表面加工和真空处理的常规方式制备三层坯料。在保护气氛中在1100℃下热轧复合材料坯料。热轧的三层坯料的厚度为1750μm。在热轧之后，将三层坯料在保护气氛中冷却至600℃持续2h。然后将坯料转移到炉中，并在氩气保护气氛中在900℃下退火3小时，并在炉中冷却。
在处理之后，将坯料在坯料长度的不同区域切割成试样以用于材料科学研究(粘合区域中的微观结构和化学元素再分布的分析)。分析结果表明，粘合的扩散过渡区的厚度为70±5μm，在粘合界面层处没有发生第二相沉淀，并且粘合界面附近的钢晶粒尺寸为65±5μm。粘合界面不含任何缺陷(裂纹、剥离等)。垂直于管壁切割的双金属显微试样的拉伸测试显示出良好的一组机械性能(σ0.2＝310±12MPa、σB＝450±15MPa和δ＝20±2％)以及它们在管长度上的更好的再现性(机械参数沿管可再现地精确至±5-7％)。因此，测试表明，使用本文公开的方法允许实现扩散过渡区的厚度的显著增加，而在粘合界面处没有复合材料组分的第二相沉淀或显著的晶粒尺寸生长。这提供了复合材料的一组改进的机械性能和管长度上的稳定的机械性质。

Claims (3)

1.一种基于钒合金和钢的制造复合材料的方法，所述复合材料包括V-(3-11wt％Ti)-(3-6wt％Cr)钒合金内层和两个含有至少13wt％铬的不锈铁素体钢外层，所述方法包括制备包括所述内层和两个外层的复合材料坯料，并进行热压处理，然后在炉中退火，其中制备所述复合材料坯料使得所述内层的厚度比所述两个不锈铁素体钢外层的总厚度大1.5-2倍，在1050-1150℃范围内进行热压处理所述复合材料坯料，然后温度降低至500-700℃,退火1-3小时，再加热至850-950℃退火，退火2-4小时并在炉中冷却，所述钒合金和钢之间形成具有60-70μm的大厚度的扩散粘合区域。
2.根据权利要求1所述的方法，其中所述热压处理是热压或热轧。
3.根据权利要求1所述的方法，其中在保护气氛中进行所述热压处理和退火。
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