CN108350557A - 铸造工具钢的活塞环及其制造工艺 - Google Patents
铸造工具钢的活塞环及其制造工艺 Download PDFInfo
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Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16J—PISTONS; CYLINDERS; SEALINGS
- F16J9/00—Piston-rings, e.g. non-metallic piston-rings, seats therefor; Ring sealings of similar construction
- F16J9/26—Piston-rings, e.g. non-metallic piston-rings, seats therefor; Ring sealings of similar construction characterised by the use of particular materials
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C4/00—Coating by spraying the coating material in the molten state, e.g. by flame, plasma or electric discharge
- C23C4/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/02—Pretreatment of the material to be coated
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
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Abstract
铸造工具钢的活塞环及其制造工艺属于用于内燃机的活塞环的工具钢的领域，涉及工具钢的铸造活塞环，其微观结构由带有具有0.5μm与2μm之间的典型尺寸并呈现高韧性的二次M2C和/或MC碳化物(M＝V和/或Mo和/或Cr和/或W)的沉淀的回火马氏体基体和体积分数在1％与4％之间，典型尺寸在3μm与7μm之间并且均匀分布的具有立方形态的NbC共晶碳化物构成，并且在回火之后，材料的硬度在400HV与800HV之间，具有根据表(I)的化学成分的极限。可以从由不同铸造工艺铸造的半成品开始获得活塞环，优选地是在湿砂或砂‑树脂的模具中铸造，在陶瓷模具中铸造和离心铸造，随后进行加工操作，并且在铸造半成品的过程中使用的原材料可以是低合金钢的废料、再循环产品和铁合金。
Description
技术领域
本发明属于用于内燃机的活塞环的领域，涉及获得包括铌、铬、钼和钒的工具钢的铸造环，包括合金的组成及其制造工艺。
背景技术
近年来，为了减少有害气体向环境的排放以及颗粒材料和/或其它GHGs(温室气体)的排放，已将一系列技术结合到发动机中。
气体排放的减少尤其与发动机的热性能的提高有关，并且因此与燃料的比耗量的减少有关。因此，发动机在气缸中的活塞的每个排量体积中产生较大的功率。在较高的旋转和较高的燃烧温度下，内燃机在较高的机械应力下工作。以这种方式，其部件的尺寸必须支持这些较苛刻的操作条件，目的在于确保组件的可靠性和预期工作寿命的保持。这种较大的操作应力同样被转化成部件(尤其是活塞和与活塞相关联的环)所经受的较大应力。
通过较大的压缩率、燃烧压力、温度和旋转，环在活塞和气缸壁上施加较大的压力，导致环较大的磨损和疲劳。
磨损和疲劳方面直接影响活塞环的耐久性，与密封性能的保持和将油膜控制在发动机的设计限制内相关。这些限制与污染物的排放、燃料消耗和润滑油消耗有关，这些都是与公共健康有关的话题。此外，较低的疲劳强度可能导致环的破裂，并因此导致发动机拉缸。除了经济重要性之外，发动机拉缸是车辆安全的基本项目。
通常用于制造活塞环的材料是铸铁和高铬马氏体钢。铸铁环的制造工艺可以概括为以下阶段：(1)合金的熔化和成分的校正；(2)倒入湿砂模具或离心；(3)对所得的环进行热处理；(4)加工以限定最终尺寸；(5)处理表面，诸如氮化或涂层，以获得具有高硬度的表面。对于在具有高负荷的发动机或需要环的小横截面尺寸的发动机中使用铸铁环，具有与机械强度有关的技术限制。
对于高负荷的应用，铸铁环由高铬马氏体钢环代替。这些通过拉拔线的机械成形获得，例如文献US20070187002(“有提高的抗擦伤性、抗裂性和抗疲劳性的活塞环，和它的生产方法，以及活塞环和气缸体的组合”)所揭示的，并且它们经历前述的阶段(4)和(5)。尽管如此，除了几何形状定义的技术缺点之外，可能通过该制造工艺产生的环的尺寸也存在限制，要求更复杂的制造和精加工工艺。为了实现多种尺寸，需要维护大量材料，增加了所涉及的成本。
与通过高铬钢的拉拔线的机械成形获得环的工艺有关的相关技术方面是微裂纹的存在，该微裂纹是由于碳化物与基体之间在轧制和拉拔阶段累积的横截面积缩减导致的剥离而产生的，特别是在其中发生碳化物结块的微观结构的区域中。这些问题是通过铸造工艺生产的高铬钢环来解决的，这些铸造工艺与用于生产铸铁环的那些铸造工艺类似。
在高铬钢的铸造环的情况下，根据文献US20120090462的描述获得的材料的微观结构呈现了在固化期间形成的粗糙的M7C3共晶碳化物。图1示出了根据文献US20120090462的实施方案的示例的描述获得的处于铸态和随后的回火状态(微观结构的发展的最后阶段)的材料的微观结构，可以观察到在枝晶间区域以连的续方式沉淀的粗糙的M7C3共晶碳化物不会随着热处理直至回火的循环的应用而改变。共晶碳化物的连续网络是用于成核和疲劳裂纹扩展的优选位点，因此其存在意味着损害活塞环的性能。
进行表面处理以获得高硬度、衬里的低磨损系数以及高耐磨性的实现对于活塞环来说是常见的。氮化是通常在活塞环上使用的表面处理工艺，通过气体、等离子体或在盐浴中实现。可选地，可以利用形成一部分现有技术的沉积材料和工艺在与气缸接触的面上施加抗磨损涂层。
附图说明
图1示出了根据文献US20120090462的实施方案的示例的描述所生产的材料在铸态(图1A)和随后600℃下的回火状态(图1B)下的微观结构。
图2呈现了在根据本发明的活塞环的熔融工具钢的凝固期间随温度变化的相位比例的发展图。
图3示出了在本发明实施方案的示例中获得的处于铸态的材料的微观结构。
图4示出了在本发明实施方案的示例中在退火(750℃下4小时并在炉中冷却)之后获得的材料的微观结构。
图5示出了在本发明实施方案的示例中在淬火(1050℃下2小时并在静止空气中冷却)之后获得的材料的微观结构。
图6示出了在本发明实施方案的示例中在回火(500℃下4小时并在静止空气中冷却)之后获得的材料的微观结构。
图7呈现了在本发明实施方案的示例中在制造过程的不同阶段中获得的材料的硬度的发展图。
图8呈现了在本发明实施方案的示例中获得的处于铸态和热处理状态(没有表面处理)的材料的滑动磨损测试结果图，将它们与机械成形和氮化高铬钢(CM)以及铸造和氮化高铬钢(F)的结果进行比较。
具体实施方式
“铸造工具钢的活塞环及其制造工艺”涉及具有高耐磨性和抗疲劳性的工具钢的铸造活塞环，然而更具体地，其涉及工具钢的铸造活塞环，其微观结构由具有二次M2C和/或MC碳化物(M＝V和/或Mo和/或Cr和/或W)的沉淀的回火马氏体基体(具有0.5μm与2μm之间的典型尺寸，呈现高韧性)和具有立方形态的NbC共晶碳化物(体积分数在1％与4％之间，典型尺寸在3μm与7μm之间并且均匀分布，在从2500到3000HV的频带中呈现高硬度)构成。这种微观结构特征为工具钢的铸造活塞环赋予高硬度、抗疲劳性和耐磨性，使其工作性能优于通过现有技术中的代表性材料(铸铁和高铬钢)制造的活塞环。此外，这种微观结构特征允许使用缺乏表面处理的工具钢的活塞环，简化其生产工艺并使其更经济。
“铸造工具钢的活塞环及其制造工艺”中包括的工具钢的化学成分基于“基体钢”的概念，最初由G.A.Roberts(Vanadium in high speed steel.Transactions of theMetallurgical Society of AIME，v.236，p.950-63，1966)限定。这个概念允许获得微观结构，其中将高硬度的基体和高硬度的共晶碳化物组合。在根据本发明的用于活塞环的铸造工具钢的情况下，根据由碳化物NbC的分子式表示的化学计量比，几乎全部铌与碳结合，这是由于奥氏体中的铌的溶解度按重量计小于0.03％。
使用ThermoCalc热力学建模软件获得的图2呈现了根据本发明的工具钢的凝固顺序。可以观察到其实际上是共晶的，液相全部分解成共晶奥氏体+NbC，并且无足轻重的部分分解成共晶奥氏体+M7C3和奥氏体+M2C。因此，对于具有按重量计3％的铌的合金，在形成按体积计3％的NbC时消耗按重量计0.39％的C，对应于按重量计每1％的Nb的0.13％的C的化学计量组合。剩余的碳量和实际上每种其它元素的全部含量将溶解在奥氏体中，并且在凝固之后和淬火和回火的热处理循环之后在冷却期间参与分解反应。
在本发明中，可以从由不同铸造工艺铸造的半成品开始获得活塞环，优选地是在湿砂或砂-树脂的模具中铸造，在陶瓷模具中铸造和离心铸造，随后进行加工操作。
在铸造半成品的过程中使用的原材料可以是低合金钢的废料、再循环产品和铁合金，但不限于这些材料。可以在感应炉中实现用于制备合金的材料的熔化，但不限于这种类型的设备。用于制备和熔化合金的炉可以具有大气和压力控制，但这些变量的控制不是严格必要的。必须在1500℃与1650℃之间的温度下实现将合金倒入到模具中。
在模具中冷却之后，如果存在浇铸通道系统，则该浇铸通道系统被移除，允许部件(环或管)的分离。在600℃与800℃之间的温度下对环或管进行退火，目的在于使材料的微观结构均化，并且便于切割和加工阶段(如果使用的话)。
在退火之后，部件经历淬火和回火的热处理，目的在于获得具有M2C和/或MC型二次碳化物和硬度在400HV与800HV之间的回火马氏体的基体。热处理由在900℃与1150℃(奥氏体化)之间的温度下加热零件以及在空气(加压的或静止的)中或在油中淬火组成。这些热处理优选地在具有受控气氛的炉中实现，以防止表面成分的变化和部件的过度氧化。在淬火热处理之后，部件可以在高达650℃的温度下经过回火阶段，以期使硬度适合所需的应用。
表1示出了构成根据本发明的用于活塞环的铸造工具钢的主要合金元素的含量的极限。
表1：工具钢成分的极限
碳和铌在工具钢的凝固期间参与NbC共晶碳化物的形成。在凝固之后的冷却期间或者在基体的马氏体回火和硬化处理期间，碳也参与M2C和/或MC型二次碳化物的沉淀。碳的最小含量确保了NbC共晶碳化物的形成，同时也确保了马氏体基体的高硬度。表1中所示的碳含量的最大极限防止了马氏体基体具有低韧性，而且还防止了工具钢过度过共晶，形成了大尺寸和树状形态的初生NbC碳化物，损害了抗疲劳性。铌的最小含量确保形成NbC的最小体积分数，以获得高硬度和耐磨性。铌含量的限制防止工具钢过度过共晶。
铬以低成本导致高淬火能力。上限确保了在凝固结束时形成无足轻重的M7C3共晶碳化物部分，防止其在枝晶间区域中以连续的方式沉淀。
元素钒、钼和钨是在回火循环期间主要负责次级M2C和/或MC碳化物的沉淀的元素，确保了基体的二次硬化。上限确保在凝固结束时形成无足轻重的M2C共晶碳化物部分，防止它们在枝晶间区域中以连续的方式沉淀。
钛在超过液相线的温度下负责Ti(C、N)碳氮化物颗粒的形成，然后作为NbC共晶碳化物的有效成核剂，并且因此促进分离和均匀分布的立方体颗粒形式的这些碳化物的沉淀。下限确保了成核剂的功能，而上限防止了氧化钛的过度形成，损害了抗疲劳性。
硅在铸造工具钢的过程中用作脱氧剂。下限确保了其脱氧功能，而上限防止其用作脆化剂。
锰在铸造工具钢的过程中用作脱氧剂，并且用作硫的中和剂，形成MnS。下限确保了其脱氧功能，而上限防止了开始形成马氏体的温度的过度降低。
磷和硫是具有脆化作用的工具钢的杂质，因此其含量必须尽可能是最低的。0.05％的上限确保了该效果没有表现出来，并且允许在工具钢的铸造中使用商业纯度的原材料。
本发明实施方案的示例
在感应炉中熔化含有低合金钢、再循环产品和铁合金的装料，不具有用于压力控制的腔室，目的在于获得根据本发明的用于活塞环的工具钢。为了防止熔融金属的过度氧化，将氩气注入到浴的表面上。在进料完全熔化和温度控制之后，在1580℃下将熔融金属倒入砂-树脂的模具中。在倒入期间，取样进行化学成分分析，结果如表2所示。
表2：在实施方案的示例中获得的样品上测得的化学成分
铸造内径和外径的尺寸接近于活塞环的尺寸的管。冷却之后，清洗管并进行退火热处理(750℃下4小时并在炉中冷却)。随后，将退火的管进行机械修整并切割成环，然后对环进行淬火(1050℃下2小时并在静止空气中冷却)和双重回火(500℃下2小时和在静止空气中冷却)的热处理。
图3示出了获得的铸造状态下的材料的微观结构，其中确定了NbC共晶碳化物。图4、图5和图6分别示出了退火、淬火和回火的热处理后材料的微观结构。
图7示出了在制造过程的每个阶段在本发明实施方案的示例中获得的材料的硬度的发展。在回火之后，硬度值为694HV，大大高于通常用于制造活塞环的铸铁和不锈钢的典型硬度值。本发明的材料的较高硬度的结果是由于其化学成分和生产过程中实现的热处理循环。
每次热处理后的硬度值和微观结构的NbC共晶碳化物的存在意味着可以利用根据本发明制造的环，而不需要现有技术中常常在活塞环上使用的材料的表面处理的阶段(氮化和陶瓷涂层)。
图8示出了在本发明实施方案的示例中获得的处于铸造和热处理(无表面处理)状态的材料的滑动磨损试验的结果，将它们与机械成形和氮化高铬钢(CM)以及铸造和氮化高铬钢(F)的结果进行比较。这些试验是在采用珠光体灰铸铁抵抗体的通用摩擦计上进行的，并且附图示出了测得的本体(环的材料)和对抗体(衬里的材料)的磨损值。
观察到，工具钢不需要氮化处理来获得与使用其它氮化材料获得的那些磨损率具有相同等级的磨损率。
Claims (10)
1.一种铸造工具钢的活塞环，其特征在于，所述铸造工具钢含有如下表所要求的化学成分的极限，并且其微观结构由带有具有少于3μm典型尺寸和高韧性的二次M2C和/或MC碳化物(M＝V和/或Mo和/或Cr和/或W)的沉淀的回火马氏体基体和体积分数在1％与4％之间，尺寸在3μm与7μm之间并且均匀分布的具有立方形态的NbC共晶碳化物构成，并且在回火之后，所述材料的硬度在400HV与800HV之间。
2.根据权利要求1所述的工艺，其特征在于，它们通过重力铸造工艺生产。
3.根据权利要求1所述的工艺，其特征在于，它们通过离心铸造工艺生产。
4.根据权利要求1和2所述的工艺，其特征在于，它们利用湿砂或砂-树脂的模具或陶瓷模具生产。
5.根据权利要求1所述的工艺，其特征在于，在所述铸造之后实现以下阶段：在600℃与800℃之间的温度下实现的退火；在900℃与1150℃之间的温度下实现的淬火热处理；在高达650℃的温度下实现的回火。
6.根据权利要求1和5所述的工艺，其特征在于，通过氮化和抗磨涂层可选地实现表面的处理。
7.根据权利要求5所述的生产工艺，其特征在于，在具有受控气氛的炉中实现所述淬火阶段。
8.根据权利要求6所述的生产工艺，其特征在于，通过气体、等离子体或在盐浴中实现所述氮化。
9.根据权利要求1所述的生产工艺，其特征在于，在与所述气缸接触的面上，通过电镀工艺或喷涂或物理气相沉积获得所述抗磨涂层。
10.根据权利要求5所述的生产工艺，其特征在于，在与所述气缸接触的面上，通过电镀工艺或喷涂或物理气相沉积获得所述抗磨涂层。
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| CN110814284A (zh) * | 2019-12-12 | 2020-02-21 | 安庆海威尔机械有限公司 | 活塞环铸造工艺 |
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| GB781027A (en) * | 1954-08-04 | 1957-08-14 | Renault | Improved process for the manufacture of piston rings |
| GB1303286A (zh) * | 1970-04-29 | 1973-01-17 | ||
| WO2012121630A1 (en) * | 2011-03-04 | 2012-09-13 | Åkers AB | A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll |
| CN103526115A (zh) * | 2013-01-29 | 2014-01-22 | 上海汇众汽车制造有限公司 | 冷作模具材料及适合于冷作模具材料的组合工艺 |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110756747A (zh) * | 2019-11-29 | 2020-02-07 | 安庆海威尔机械有限公司 | 活塞环砂型成型方法 |
| CN110814284A (zh) * | 2019-12-12 | 2020-02-21 | 安庆海威尔机械有限公司 | 活塞环铸造工艺 |
| CN110814284B (zh) * | 2019-12-12 | 2020-11-17 | 安庆海威尔机械有限公司 | 活塞环铸造工艺 |
Also Published As
| Publication number | Publication date |
|---|---|
| US20180313447A1 (en) | 2018-11-01 |
| US10309536B2 (en) | 2019-06-04 |
| BR102015027438B1 (pt) | 2020-11-17 |
| DE112016004959T5 (de) | 2018-07-26 |
| WO2017072075A1 (en) | 2017-05-04 |
| BR102015027438B8 (pt) | 2021-12-21 |
| CN108350557B (zh) | 2020-05-12 |
| BR102015027438A2 (pt) | 2017-07-18 |
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