WO2021103843A1 - 一种激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层及其制备方法 - Google Patents

一种激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层及其制备方法 Download PDF

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WO2021103843A1
WO2021103843A1 PCT/CN2020/121729 CN2020121729W WO2021103843A1 WO 2021103843 A1 WO2021103843 A1 WO 2021103843A1 CN 2020121729 W CN2020121729 W CN 2020121729W WO 2021103843 A1 WO2021103843 A1 WO 2021103843A1
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entropy alloy
composite layer
alcocrfeni
alloy alcocrfeni
steel composite
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PCT/CN2020/121729
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English (en)
French (fr)
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樊宇
宋之克
张军
方荣超
丁贺
李永超
范鹏
安泽
张李祥
徐杰
陈正
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中国矿业大学
徐州徐工挖掘机械有限公司
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Publication of WO2021103843A1 publication Critical patent/WO2021103843A1/zh

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/346—Working by laser beam, e.g. welding, cutting or boring in combination with welding or cutting covered by groups B23K5/00 - B23K25/00, e.g. in combination with resistance welding
    • B23K26/348—Working by laser beam, e.g. welding, cutting or boring in combination with welding or cutting covered by groups B23K5/00 - B23K25/00, e.g. in combination with resistance welding in combination with arc heating, e.g. TIG [tungsten inert gas], MIG [metal inert gas] or plasma welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/0093—Working by laser beam, e.g. welding, cutting or boring combined with mechanical machining or metal-working covered by other subclasses than B23K
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/12—Working by laser beam, e.g. welding, cutting or boring in a special atmosphere, e.g. in an enclosure
    • B23K26/1224—Working by laser beam, e.g. welding, cutting or boring in a special atmosphere, e.g. in an enclosure in vacuum
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
    • B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass

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  • the invention relates to the field of welding, in particular to a high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer and a preparation method thereof.
  • the working conditions of the hydraulic support column are harsh, mainly working under heavy load, vibration, impact, friction and medium corrosion.
  • the entire equipment is surrounded by dust, water vapor and harmful gases, and the lubrication conditions are poor.
  • the main failure modes of the hydraulic support column are corrosion and wear, so the surface treatment technology of the column is a key factor affecting the service life of the hydraulic support.
  • the first generation of column surface treatment technology is chromium electroplating and chemical plating technology, which not only produces electroplating wastewater containing heavy metal ions and various acid mist exhaust gas, but also causes great health hazards to the operators and serious environmental pollution, which affects the service life of the columns. Increasing the overall maintenance cost of the hydraulic support will endanger the safety of the hydraulic support product.
  • the second-generation column surface treatment technology is plasma spraying and laser cladding technology, using alloy powder as raw material, powder production has a series of shortcomings such as high cost and long cycle, and powder processing is prone to defects such as pores and cracks, hot processing process Residual stress is easy to produce. In addition, suspended particles in the air will increase during the production process, which is very harmful to the health of the operators.
  • the technical problem to be solved by the present invention is to overcome the defects of the prior art and provide a laser cladding welding technology to repair the hydraulic support: laser welding is used instead of laser cladding, and thin plate strips are used instead of alloy powder to repair the surface of the hydraulic support column.
  • the present invention provides a method for preparing a laser clad welding high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer, which includes the following steps:
  • Step one prepare high-entropy alloy AlCoCrFeNi raw materials, put the high-entropy alloy AlCoCrFeNi raw materials into the smelting furnace, use an exhaust system to pump the vacuum to within 5 ⁇ 10 -3 Pa, then close the exhaust system and fill with argon until the pressure Close the charging system after 0.01atm, and repeat the pumping and charging operation more than three times to ensure the high vacuum in the furnace;
  • Step 2 Adjust the smelting arc gun to just above the high-entropy alloy AlCoCrFeNi raw material, ensure that the tip of the gun is 3 to 4 mm away from the raw material, turn on the power to start melting; keep the arc for 3 to 5 minutes, turn off the power, and let the high-entropy alloy AlCoCrFeNi raw material cool in circulating water The crucible is naturally cooled; turn the high-entropy alloy AlCoCrFeNi raw material over and continue smelting;
  • Step 3 Process the melted high-entropy alloy AlCoCrFeNi into metal flakes, cover the metal flakes on the 27SiMn steel cylinder, and use laser welding to perform multi-pass lap welding on the metal flakes and the cylinder;
  • Step 4 Extruding the metal flakes to bond the metal flakes to the cylindrical barrel, and perform diameter reduction and fusion until a fusion boundary is formed between the metal flakes and the cylindrical barrel to obtain a high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer.
  • step one the molar ratio of each substance in the high-entropy alloy AlCoCrFeNi is 1:1:1:1:1.
  • step 2 the number of smelting is 5-6 times, each time is 5-8 minutes.
  • step three the laser power of the laser welding is 600W, and the speed is 1.6m/min. Under this condition, the surface of the composite layer prepared by laser cladding welding is relatively flat and the structure is compact.
  • step 4 the step of reducing the diameter is: extruding the metal flake with a reducing die to make the thickness of the metal flake less than the thickness of the cylindrical barrel 0.2-0.3 mm.
  • the fusion step is: heating the entire metal sheet to 400-500°C, and then applying pressure from one end of the metal sheet to 40-45 MPa to the other end of the metal sheet to complete the fusion.
  • the fusion step is: heating one end of the metal flake to 400-500°C while applying pressure to 40-45 MPa, and gradually implement the above operation to the other end of the metal flake to complete the fusion.
  • step five surface hardening: nitriding the surface of the high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer; the parameters are: the temperature is 380-400°C, the nitriding is 3 to 4 hours, and the heat preservation is 5 to 6 hours;
  • step 6 polishing: polishing the outer circle of the high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer, and the polishing time is 15-20 minutes.
  • the invention also provides a high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer prepared by laser cladding welding, which is prepared according to the above preparation method.
  • the beneficial effect of the present invention is that the present invention adopts the laser cladding welding method to prepare the high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer, and obtains a well-shaped, uniform and compact welding structure, which is for the field of laser welding of high-entropy alloy composite layers.
  • the yield stress of the composite layer prepared by the invention is greater than that of the high-entropy alloy AlCoCrFeNi base material.
  • the friction coefficient of the composite layer is smaller than that of the high-entropy alloy AlCoCrFeNi base material, and the wear amount is also smaller than that of the high-entropy alloy AlCoCrFeNi base material and the 27SiMn steel matrix.
  • the composite layer has better wear resistance.
  • the self-corrosion potential of the composite layer is greater than the high-entropy alloy AlCoCrFeNi base material and the 27SiMn steel matrix, and its self-corrosion current density is the smallest, and the composite layer has more excellent corrosion resistance.
  • Figure 1 shows the yield stress diagram of the composite layer under different laser welding parameters: (a) laser power, (b) welding speed;
  • Figure 2 is a comparison diagram of composite layer wear under different parameters: (a) laser power, (b) welding speed.
  • a method for preparing a high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer by laser cladding welding includes the following steps:
  • Step 1 Select the granular bulk metal with a purity of 99.99wt.%, according to the designed atomic ratio of the alloy, with the total mass of the alloy as the standard of 100g, select the processed metal particles of each element as the raw material, and the accuracy can reach 4 decimal places. Analytical balance weighs the required mass of each element in turn, the specific mass is shown in Table 1;
  • Step 2 Ensure the normal operation of the circulating water cooling system and the power system, adjust the melting arc gun to the crucible where the raw material is located, ensure that the gun tip is about 3mm away from the raw material, turn on the power, and start melting.
  • the arc gun rocker By controlling the arc gun rocker to ensure that the raw materials are always within the melting range of the arc and the size of the melting current is adjusted, the raw materials to be smelted are fully melted, the arc is maintained for a period of time, the power is turned off, and it is naturally cooled in the circulating water-cooled crucible.
  • Use the turning spoon equipped with the equipment to turn the raw materials over and continue smelting. If you want to obtain a high-entropy alloy ingot with uniform composition, the number of smelting times for each sample is 5 times, each time is 5 minutes.
  • Step 3 Use a wire cutting machine to process the melted high-entropy alloy AlCoCrFeNi round cake-shaped ingot into 1mm metal flakes.
  • the metal flakes are covered on a 27SiMn steel cylinder for laser welding and multiple lap welding.
  • the dimensions of the 27SiMn steel cylinder are: the outer diameter is 100mm, the inner diameter is 90mm, and the height is 195mm.
  • Step 4 Extrusion of the metal sheet to bond the metal sheet to the cylinder, and reduce the diameter to make the thickness of the metal sheet less than the thickness of the cylinder 0.2mm; then perform fusion, and heat one end of the metal sheet to 400-500°C, Simultaneously apply pressure to 40-45 MPa, and gradually implement the above operations to the other end of the metal sheet until a fusion junction is formed between the metal sheet and the cylinder, and a high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer is prepared.
  • Step 5 Surface hardening: Nitriding treatment is performed on the surface of the high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer; the parameters are: the temperature is 380°C, the nitriding is 3 hours, and the heat preservation is 5 hours.
  • Step 6 Polishing: Polish the outer circle of the high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer for 15 minutes.
  • the nano-mechanics comprehensive test system is used to perform nano-indentation test on the high-entropy alloy AlCoCrFeNi/27SiMn steel composite layer prepared by laser cladding welding, which can directly measure the maximum indentation depth of the composite layer, the maximum load and other physical quantities, which can be obtained by calculation
  • the theoretical yield stress of the surface of the composite layer as shown in Figure 1, the average yield stress of the welded composite layer is 608.08 ⁇ 36.24MPa, the yield stress of the high-entropy alloy AlCoCrFeNi as-cast base material is 482.38 ⁇ 19.62MPa, the yield stress of the base material is obvious It is less than the yield stress of the welded composite layer.
  • the structure of the composite layer is more refined, and the crystal grains are finer.
  • the refinement of the crystal grains makes the grains in the same area more and more grain boundaries, which hinders The stronger the dislocation slip ability, the stronger the ability to resist plastic deformation, so the refinement of the crystal grains will hinder the generation of deformation and increase the surface yield stress of the welded composite layer.
  • the changes of laser power and welding speed have little effect on the surface yield stress of the composite layer prepared by laser cladding welding.
  • the yield stress of the welded composite layer reaches the maximum value at 1050W and 1.6m/min, which is 630.16 ⁇ 38.12MPa.
  • Figure 2 is a histogram of the wear volume of the AlCoCrFeNi/27SiMn steel welded composite layer under different process parameters. It can be seen from the figure (a) that the greater the laser power, the smaller the wear of the welded composite layer. When the laser power reaches the maximum 1050W, the wear of the welded composite layer is the smallest, which is about 7.65 ⁇ 0.32mg. When the power is 300W, the maximum amount of wear is about 8.41 ⁇ 0.35mg, but it is still less than the amount of wear of the high-entropy alloy AlCoCrFeNi as-cast base material 8.62 ⁇ 0.41mg, which proves that the wear resistance of the welded composite layer is better than that of high-entropy alloy.
  • the figure is a histogram of the wear amount of the welded composite layer obtained at different welding speeds. It can be seen from the figure that when the welding speed is 1.8m/min, the wear amount of the composite layer is the largest, about 8.32 ⁇ 0.51mg When the welding speed is 1.2m/min, the wear amount of the composite layer is the smallest, about 7.74 ⁇ 0.46mg. During the welding speed change, the wear amount only changes by 0.61mg, which is very small.
  • the characteristic values of the polarization curve self-corrosion current density (Icorr) and self-corrosion potential (Ecorr) can be obtained, as shown in Table 2. It can be seen from the comparison of the values in the table that the self-corrosion potential of the welded composite layer is the highest, indicating that it has no tendency to preferentially corrode and its self-corrosion current density is the smallest.
  • the self-corrosion current is the corrosion current when the electrode is in an open state, and its value is The smaller the value, the better the corrosion resistance of the material. It can be concluded that the corrosion resistance of the welded composite layer is better than that of the high-entropy alloy AlCoCrFeNi base material and the 27SiMn steel matrix.

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Abstract

一种激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，包括以下步骤：1)配制高熵合金AlCoCrFeNi原料，将原料放入熔炼炉，采用抽气系统将真空度抽至5×10 -3Pa以内，随后关闭抽气系统并充入氩气直到压力为0.01atm；2)将熔炼电弧枪调节至原料正上方熔炼，之后让原料冷却；3)将熔炼出的高熵合金AlCoCrFeNi加工成为金属薄片，将金属薄片覆盖在27SiMn钢圆柱筒上，采用激光焊接对金属薄片和圆柱筒进行多道搭接焊；4)对金属薄片进行挤压，使金属薄片与圆柱筒贴合，进行缩径、熔合，制得高熵合金AlCoCrFeNi/27SiMn钢复合层。采用上述方法制得的复合层的屈服应力大于高熵合金AlCoCrFeNi母材，复合层的摩擦系数小于高熵合金AlCoCrFeNi母材，复合层的耐磨性能、耐腐蚀性更加优异。

Description

一种激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层及其制备方法 技术领域
本发明涉及焊接领域，尤其是一种高熵合金AlCoCrFeNi/27SiMn钢复合层及其制备方法。
背景技术
液压支架立柱的工况条件苛刻，主要是在重载、振动、冲击、摩擦和介质腐蚀等条件下工作。此外，整体设备处于粉尘、水汽及有害气体的包围中，润滑条件差。液压支架立柱的主要失效形式是腐蚀与磨损，因此立柱的表面处理技术是影响液压支架使用寿命的关键因素。
第一代立柱表面处理技术为电镀铬与化学镀技术，不仅会产生含重金属离子的电镀废水和各类酸雾废气，对操作工人的健康危害极大，环境污染十分严重，影响立柱使用寿命，增加液压支架整体维护成本，严重则将危及液压支架产品的使用安全性。
第二代立柱表面处理技术为等离子喷涂与激光熔覆技术，采用合金粉末作为原材料，粉末制作存在成本高、周期长等一系列的缺点，且粉末加工容易出现气孔、裂纹等缺陷，热加工过程易产生残余应力，此外生产过程中，空气中悬浮颗粒物会增多，对操作工人的健康危害很大。
发明内容
本发明所要解决的技术问题在于克服现有技术缺陷，提供一种激光包覆焊技术来修复液压支架：用激光焊接代替激光熔覆，薄板带材代替合金粉末，对液压支架立柱表面进行修复。
为了解决上述技术问题，本发明提供一种激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，包括以下步骤：
步骤一，配制高熵合金AlCoCrFeNi原料，将高熵合金AlCoCrFeNi原料放入熔炼炉，采用抽气系统将真空度抽至5×10 -3Pa以内，随后关闭抽气系统并充入氩气直到压力为0.01atm后关闭充气系统，重复抽充气操作三次以上，以确保炉内的高真空度；
步骤二，将熔炼电弧枪调节至高熵合金AlCoCrFeNi原料正上方，保证枪尖距离原料3～4mm，打开电源，开始熔炼；电弧保持3～5分钟，关闭电源，让高熵合金AlCoCrFeNi原料在循环水冷坩埚内自然冷却；将高熵合金AlCoCrFeNi原料翻面，继续熔炼；
步骤三，将熔炼出的高熵合金AlCoCrFeNi加工成为金属薄片，将金属薄片覆盖在27SiMn钢圆柱筒上，采用激光焊接对金属薄片和圆柱筒进行多道搭接焊；
步骤四，对金属薄片进行挤压，使金属薄片与圆柱筒贴合，进行缩径、熔合，直至金属薄片和圆柱筒之间产生熔合结界，制得高熵合金AlCoCrFeNi/27SiMn钢复合层。
作为改进，在步骤一中，高熵合金AlCoCrFeNi中各物质的摩尔比为1:1:1:1:1。
作为改进，在步骤二中，熔炼的次数为5～6次，每次5～8分钟。
作为改进，在步骤三中，激光焊接的激光功率采用600W，速度采用1.6m/min。该条件下通过激光包覆焊接制备出的复合层表面较为平整，结构致密。
作为改进，在步骤四中，缩径的步骤为：用缩径模具挤压金属薄片，使金属薄片厚度小于圆柱筒厚度0.2～0.3mm。
作为改进，在步骤四中，熔合的步骤为：将整个金属薄片加热至400～500℃，然后从金属薄片的一端开始施加压力至40～45MPa直至金属薄片的另一端，完成熔合。
作为改进，在步骤四中，熔合的步骤为：将金属薄片的一端加热至400～500℃、同时施加压力至40～45MPa，逐步实施上述操作至金属薄片的另一端，完成熔合。
作为改进，还包括步骤五：表面硬化：对高熵合金AlCoCrFeNi/27SiMn钢复合层表面进行氮化处理；参数为：温度为380～400℃，氮化3～4小时，保温5～6小时；
作为改进，还包括步骤六：抛光：对高熵合金AlCoCrFeNi/27SiMn钢复合层外圆进行抛光，抛光时间为15～20min。
本发明还提供一种激光包覆焊接制备高熵合金AlCoCrFeNi/27SiMn钢复合层，根据以上制备方法制得。
本发明的有益效果在于：本发明采用激光包覆焊接的方法制备高熵合金AlCoCrFeNi/27SiMn钢复合层，获得了表面成形良好，均匀致密的焊接组织，是为激光焊接高熵合金复合层领域进行了初步的探索。本发明制得的复合层的屈服应力大于高熵合金AlCoCrFeNi母材。复合层的摩擦系数小于高熵合金AlCoCrFeNi母材，磨损量也小于高熵合金AlCoCrFeNi母材和27SiMn钢基体，复合层的耐磨性能更加优异。复合层的自腐蚀电位大于高熵合金AlCoCrFeNi母材和27SiMn钢基体且其自腐蚀电流密度最小，复合层的耐腐蚀性更加优异。
附图说明
图1为不同激光焊接参数下复合层屈服应力图:(a)激光功率,(b)焊接速度；
图2为不同参数下复合层磨损量对比图:(a)激光功率,(b)焊接速度。
具体实施方式
下面将结合附图对本发明作详细说明。
一种激光包覆焊接制备高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，包括以下步骤：
步骤一：选用纯度为99.99wt.％粒状块体金属，按照合金设计的原子比，以合金总质量100g作为标准，选用处理好的各元素金属粒作为原料，使用精度可达到小数点后4位的分析天平依次称取各元素所需质量，具体质量见表1；
表1高熵合金AlCoCrFeNi的组成成分
成分 Co Cr Al Fe Ni
质量(g) 23.34 20.60 10.69 22.12 23.25
原料放入坩埚后，使真空电弧熔炼炉保持密闭，使用机械泵进行预抽至20Pa，然后用分子泵抽真空到炉内气压为5×10 -3Pa以内，关闭分子泵，充入高纯气体Ar，直到压力为0.01atm，关闭充气系统，重复上述操作三次以确保炉内的高真空度。
步骤二：确保循环水冷却系统和动力系统正常运行，将熔炼电弧枪调节至原料所在的坩埚正上方，保证枪尖距离原料约3mm，打开电源，开始熔炼。通过控制电弧枪摇杆来确保原料始终在电弧的熔炼范围内以及调节熔炼电流的大小，使要熔炼的原料充分熔化，电弧保持一段时间，关闭电源，使之在循环水冷坩埚内自然冷却。使用设备配备的翻转勺将原料翻面，继续熔炼，如果想要获得成分均匀的高熵合金铸锭，每个试样熔炼次数为5次，每次5分钟。
步骤三：使用线切割机将熔炼出高熵合金AlCoCrFeNi圆饼状铸锭加工成为1mm金属薄片。将金属薄片覆盖在27SiMn钢圆柱筒进行激光焊接，进行多道搭接焊；27SiMn钢圆柱筒的尺寸为：外径为100mm、内径为90mm，高为195mm。
步骤四：对金属薄片进行挤压，使金属薄片与圆柱筒贴合，进行缩径，使金属薄片厚度小于圆柱筒厚度0.2mm；然后进行熔合，将金属薄片的一端加热至400～500℃、同时施加压力至40～45MPa，逐步实施上述操作至金属薄片的另一端，直至金属薄片和圆柱筒之间产生熔合结界，制得高熵合金AlCoCrFeNi/27SiMn钢复合层。
步骤五：表面硬化：对高熵合金AlCoCrFeNi/27SiMn钢复合层表面进行氮化处理；参数为：温度为380℃，氮化3小时，保温5小时。
步骤六：抛光：对高熵合金AlCoCrFeNi/27SiMn钢复合层外圆进行抛光15min。
对激光包覆焊接制备高熵合金AlCoCrFeNi/27SiMn钢复合层的力学性能、耐磨性能 和耐腐蚀性能进行测试分析。
使用纳米力学综合测试系统对激光包覆焊接制备的高熵合金AlCoCrFeNi/27SiMn钢复合层进行纳米压痕试验，可以直接测出复合层的最大压入深度，最大承受载荷等物理量，通过计算得出复合层表面的理论屈服应力，如图1所示，焊接复合层的平均屈服应力为608.08±36.24MPa，高熵合金AlCoCrFeNi铸态母材的屈服应力为482.38±19.62MPa，母材的屈服应力明显小于焊接复合层的屈服应力，这是因为相较于母材，复合层的组织更加细化，晶粒细小，晶粒的细化使得相同区域内晶粒变多，晶界也变多，阻碍位错滑移的能力就越强，抵抗塑性变形的能力也就越强，所以晶粒的细化会阻碍变形的产生从而增大焊接复合层的表面屈服应力。激光功率和焊接速度的变化对激光包覆焊接制备的复合层的表面屈服应力影响不大，焊接复合层的屈服应力在1050W，1.6m/min的参数下达到最大值，为630.16±38.12MPa。
图2是不同工艺参数下AlCoCrFeNi/27SiMn钢焊接复合层磨损量柱状图。从(a)图中可以看出，激光功率越大，焊接复合层的磨损量越小，当激光功率达到最大的1050W时，焊接复合层的磨损量最小，约为7.65±0.32mg，在激光功率为300W时，磨损量最大约为8.41±0.35mg，但仍然小于高熵合金AlCoCrFeNi铸态母材的磨损量8.62±0.41mg，从另一个方面证明了焊接复合层的耐磨性能优于高熵合金AlCoCrFeNi母材。(b)图为不同焊接速度下获得的焊接复合层的磨损量柱状图，从图中可以看出，在焊接速度为1.8m/min时，复合层的磨损量最大，约为8.32±0.51mg，在焊接速度为1.2m/min时，复合层的磨损量最小，约为7.74±0.46mg，在焊接速度的变化过程中，磨损量仅变化了0.61mg，变化范围很小。
使用用塔菲尔直线外推与腐蚀电位相交可以得到极化曲线的特征值自腐蚀电流密度(Icorr)和自腐蚀电位(Ecorr)，如表2所示。从表里数值的对比可以看出，焊接复合层的自腐蚀电位最高，说明其没有优先腐蚀的倾向，且其自腐蚀电流密度最小，自腐蚀电流是电极处于开路状态时的腐蚀电流，其数值越小，表示材料的耐腐蚀性能越好，由此可以得出，焊接复合层的耐腐蚀性要好于高熵合金AlCoCrFeNi母材以及27SiMn钢基体。
表2极化曲线特征值。
Figure PCTCN2020121729-appb-000001
以上所述仅是本发明的优选实施方式，应当指出，对于本技术领域的普通技术人员来说，在不脱离本发明原理的前提下还可以做出若干改进，这些改进也应视为本发明的保护 范围。

Claims (10)

  1. 一种激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于包括以下步骤：
    步骤一，配制高熵合金AlCoCrFeNi原料，将高熵合金AlCoCrFeNi原料放入熔炼炉，采用抽气系统将真空度抽至5×10 -3Pa以内，随后关闭抽气系统并充入氩气直到压力为0.01atm后关闭充气系统，重复抽充气操作三次以上；
    步骤二，将熔炼电弧枪调节至高熵合金AlCoCrFeNi原料正上方，保证枪尖距离原料3～4mm，打开电源，开始熔炼；电弧保持3～5分钟，关闭电源，让高熵合金AlCoCrFeNi原料在循环水冷坩埚内自然冷却；将高熵合金AlCoCrFeNi原料翻面，继续熔炼；
    步骤三，将熔炼出的高熵合金AlCoCrFeNi加工成为金属薄片，将金属薄片覆盖在27SiMn钢圆柱筒上，采用激光焊接对金属薄片和圆柱筒进行多道搭接焊；
    步骤四，对金属薄片进行挤压，使金属薄片与圆柱筒贴合，进行缩径、熔合，直至金属薄片和圆柱筒之间产生熔合结界，制得高熵合金AlCoCrFeNi/27SiMn钢复合层。
  2. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：在步骤一中，所述高熵合金AlCoCrFeNi中各物质的摩尔比为1:1:1:1:1。
  3. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：在步骤二中，所述熔炼的次数为5～6次，每次5～8分钟。
  4. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：在步骤三中，所述激光焊接的激光功率采用600W，速度采用1.6m/min。
  5. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：在步骤四中，缩径的步骤为：用缩径模具挤压金属薄片，使金属薄片厚度小于圆柱筒厚度0.2～0.3mm。
  6. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：在步骤四中，熔合的步骤为：将整个金属薄片加热至400～500℃，然后从金属薄片的一端开始施加压力至40～45MPa直至金属薄片的另一端，完成熔合。
  7. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：在步骤四中，熔合的步骤为：将金属薄片的一端加热至400～500℃、同时施加压力至40～45MPa，逐步实施上述操作至金属薄片的另一端，完成熔合。
  8. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：还包括步骤五：表面硬化：对高熵合金AlCoCrFeNi/27SiMn钢复合层表面进行氮化处理；参数为：温度为380～400℃，氮化3～4小时，保温5～6小时。
  9. 根据权利要求1所述的激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法，其特征在于：还包括步骤六：抛光：对高熵合金AlCoCrFeNi/27SiMn钢复合层外圆进行抛光，抛光时间为15～20min。
  10. 一种激光包覆焊接制备高熵合金AlCoCrFeNi/27SiMn钢复合层，其特征在于：根据权利要求1-9任一项激光包覆焊接高熵合金AlCoCrFeNi/27SiMn钢复合层的制备方法制得。
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