WO2022227160A1 - 一种控轧加高温回火的齿轮钢棒材 - Google Patents

一种控轧加高温回火的齿轮钢棒材 Download PDF

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WO2022227160A1
WO2022227160A1 PCT/CN2021/096016 CN2021096016W WO2022227160A1 WO 2022227160 A1 WO2022227160 A1 WO 2022227160A1 CN 2021096016 W CN2021096016 W CN 2021096016W WO 2022227160 A1 WO2022227160 A1 WO 2022227160A1
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high temperature
steel bar
gear steel
temperature tempering
rolling
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PCT/CN2021/096016
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English (en)
French (fr)
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王莹
李海洋
周蕾
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南京钢铁股份有限公司
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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
    • C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a controlled rolling and high temperature tempering gear steel bar, in particular to a controlled rolling and high temperature tempering gear steel bar with good microstructure uniformity and purity.
  • Cold forging is the forming process of the material below the recrystallization temperature, and the forging is carried out below the recovery temperature. In production, forging without heating the blank is called cold forging. Most of the cold forging materials are aluminum and some alloys, copper and some alloys, low carbon steel, medium carbon steel, and low alloy structural steel with low deformation resistance and good plasticity at room temperature. Cold forgings have good surface quality and high dimensional accuracy, which can replace some cutting processes. Cold forging can strengthen the metal and increase the strength of the part.
  • Gear steel currently used for cold precision forging needs spheroidizing annealing or isothermal annealing treatment before cold forging, but spheroidizing annealing or isothermal annealing requires a long treatment time and high cost.
  • the present invention aims to provide a gear steel bar with controlled rolling and high temperature tempering, so as to solve the problems of long cycle and high cost of existing spheroidizing annealing or isothermal annealing.
  • the controlled rolling and high temperature tempering gear steel bar according to the present invention includes the following components according to weight percentage: C: 0.15-0.25%, Mn: 1.00-1.50%, Si ⁇ 0.35%, P ⁇ 0.030%, S ⁇ 0.030%, Cr: 1.00-1.50%, Al: 0.010-0.045%, and the rest are Fe and inevitable impurities.
  • a preparation method of a gear steel bar with controlled rolling and high temperature tempering comprising the following steps:
  • Step 1 heating the bar for gear steel
  • Step 2 Dephosphorization of billet
  • Step 3 Two-fire rolling and heating
  • Step 4 Phosphorus removal by second fire rolling
  • Step 5 Finish rolling temperature
  • Step 6 High temperature tempering
  • Step 7 Ultrasonic flaw detection, magnetic flux leakage flaw detection.
  • the temperature of the blank heating is 950-1270° C.
  • the total heating time of the blank heating is ⁇ 240 min.
  • the dephosphorization of the billet is descaled by high-pressure water, and the pressure is greater than or equal to 13MPa.
  • the heating temperature of the second-fire rolling is 980°C-1240°C, and the total heating time is ⁇ 180min.
  • step 4 high-pressure water descaling is used for the dephosphorization of the second-fire rolling, and the pressure is ⁇ 13MPa.
  • the finish rolling temperature is less than or equal to 1000°C.
  • the high temperature tempering adopts the high temperature tempering in a roller hearth continuous furnace, the temperature is 620-680°C, and the holding time of the high temperature section is set, and the holding time of the high temperature section is ⁇ 2h.
  • the ultrasonic flaw detection accuracy meets the A-level requirements of GB4162, and the surface defect depth is less than or equal to 0.30mm.
  • gear steel bar used in the step 1 includes the following components according to weight percentage:
  • the present invention has the following significant advantages: 1. It has good uniformity and purity of the structure; 2.
  • the structure is ferrite + pearlite, the bainite content is less than or equal to 3%, and the steel is pure Degree K3 ⁇ 20, hardness ⁇ 180HBW, hardness dispersion ⁇ 20HBW, surface defect depth ⁇ 0.30mm, surface decarburization layer ⁇ 0.40mm; 3. It has excellent cold forging performance and performance.
  • Fig. 1 is the metallographic structure diagram after the high temperature tempering of the present invention
  • Fig. 2 is the depth map of the surface decarburization layer of the present invention.
  • the controlled rolling and high temperature tempering gear steel bar described in this embodiment includes the following components by weight: C: 0.15-0.25%, Mn: 1.00-1.50%, Si ⁇ 0.35%, P ⁇ 0.030%, S ⁇ 0.030%, Cr: 1.00-1.50%, Al: 0.010-0.045%, and the rest are Fe and inevitable impurities.
  • a preparation method of a gear steel bar with controlled rolling and high temperature tempering comprising the following steps:
  • Step 1 billet heating for gear steel bars
  • Step 2 billet dephosphorization
  • Step 3 Second-fire rolling and heating
  • Step 4 Second-fire rolling for phosphorus removal
  • Step 5 Finish rolling temperature
  • Step 6 High temperature tempering
  • Step 7 Ultrasonic flaw detection, magnetic flux leakage flaw detection.
  • step 1 the temperature of the blank heating is 950-1270° C., and the total heating time of the blank heating is ⁇ 240 min.
  • step 2 the dephosphorization of the billet is descaled by high-pressure water, and the pressure is greater than or equal to 13MPa.
  • step 3 the heating temperature of the second-fire rolling is 980°C-1240°C, and the total heating time is ⁇ 180min.
  • step 4 the dephosphorization of the second fire rolling adopts high-pressure water descaling, and the pressure is greater than or equal to 13MPa.
  • step 5 the finishing rolling temperature is less than or equal to 1000°C.
  • step 6 the high temperature tempering adopts the high temperature tempering in a roller hearth continuous furnace, the temperature is 620-680°C, and the holding time of the high temperature section is set, and the holding time of the high temperature section is ⁇ 2h.
  • step 7 the ultrasonic flaw detection accuracy meets the A-level requirements of GB4162, and the surface defect depth is less than or equal to 0.30mm.
  • the bar for gear steel used in step 1 includes the following components by weight:
  • This embodiment adopts the specific composition of the gear steel bar for cold forging with a specification of ⁇ 20-80mm, as shown in Table 1 (unit: %):
  • Step 1 Blank heating: Blank heating temperature: 950-1270°C, total heating time ⁇ 240min;
  • Step 2 Dephosphorization of billet: Descale with high pressure water, pressure ⁇ 13MPa;
  • Step 3 Second-fire rolling heating: Second-fire rolling heating temperature: 980°C-1240°C, total heating time ⁇ 180min;
  • Step 4 Phosphorus removal by second fire rolling: use high-pressure water for descaling, pressure ⁇ 13MPa;
  • Step 5 Finishing rolling temperature: finishing rolling temperature ⁇ 1000°C;
  • Step 6 High temperature tempering: high temperature tempering in roller hearth continuous furnace, high temperature tempering temperature 620-680 °C, holding time in high temperature section ⁇ 2h;
  • Step 7 Ultrasonic flaw detection and magnetic flux leakage flaw detection: Ultrasonic flaw detection accuracy meets the requirements of Grade A of GB4162, and the depth of surface defects is ⁇ 0.30mm.
  • tissue type, purity, hardness and depth of decarburization layer are selected as follows:
  • the structure is ferrite + pearlite, and the bainite content is ⁇ 3%, see Figure 1.
  • the hardness after high temperature tempering is 160HBW, and the hardness difference is 15HBW.
  • the surface decarburization layer is 0.35mm, see Figure 2.
  • the bar of the present invention can fully meet the cold precision forging requirements of downstream customers. After the customer is cold forged into gears, various properties are good and fully meet the use requirements.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
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Abstract

本发明公开了一种控轧加高温回火的齿轮钢棒材，按照重量百分比包括以下组分：C：0.15-0.25％、Mn：1.00-1.50％、Si≤0.35％、P≤0.030％、S≤0.030％、Cr：1.00-1.50％、Al：0.010-0.045％，其余为Fe和不可避免的杂质。

Description

一种控轧加高温回火的齿轮钢棒材 技术领域
本发明涉及一种控轧加高温回火的齿轮钢棒材，尤其涉及一种具有良好的组织均匀性及纯净度的控轧加高温回火的齿轮钢棒材。
背景技术
冷锻是对物料再结晶温度以下的成型加工，是在回复温度以下进行的锻造。生产中习惯把不加热毛坯进行的锻造称为冷锻。冷锻材料大都是室温下变形抗力较小、塑性较好的铝及部分合金、铜及部分合金、低碳钢、中碳钢、低合金结构钢。冷锻件表面质量好，尺寸精度高，能代替一些切削加工。冷锻能使金属强化，提高零件的强度。
目前使用于冷精锻的齿轮钢，在冷锻前需要球化退火或者等温退火处理，但是球化退火或等温退火需要处理的时间长，成本比较高。
发明内容
发明目的：本发明旨在提供一种控轧加高温回火的齿轮钢棒材，解决现有球化退火或等温退火周期长、成本高的问题。
技术方案：本发明所述的控轧加高温回火的齿轮钢棒材，包括按照重量百分比包括以下组分：C：0.15-0.25％、Mn：1.00-1.50％、Si≤0.35％、P≤0.030％、S≤0.030％、Cr：1.00-1.50％、Al：0.010-0.045％，其余为Fe和不可避免的杂质。
一种控轧加高温回火的齿轮钢棒材的制备方法，包括以下步骤：
步骤1：对齿轮钢用棒材开坯加热；
步骤2：开坯除磷；
步骤3：二火轧制加热；
步骤4：二火轧制除磷；
步骤5：终轧温度；
步骤6：高温回火；
步骤7：超声波探伤、漏磁探伤。
进一步的，所述步骤1中，所述开坯加热的温度：950-1270℃，开坯加热的总加热时间≥240min。
进一步的，所述步骤2中，所述开坯除磷采用高压水除鳞，压力≥13MPa。
进一步的，所述步骤3中，所述二火轧制加热温度为980℃-1240℃，总加热时间≥180min。
进一步的，所述步骤4中，所述二火轧制除磷采用高压水除鳞，压力≥13MPa。
进一步的，所述步骤5中，所述终轧温度≤1000℃。
进一步的，所述步骤6中，所述高温回火采用辊底式连续炉高温回火，温度为620-680℃，并设置高温段的保温时间，所述高温段保温时间≥2h。
进一步的，所述步骤7中，所述超声波探伤精度满足GB4162的A级要求，表面缺陷深度≤0.30mm。
进一步的，所述步骤1中使用的齿轮钢用棒材，按照重量百分比包括以下组分：
C：0.20％、Mn：1.25％、Si：0.11％、P：0.010％、S：0.005％、Cr：1.13％、Al：0.021％，其余为Fe和不可避免的杂质。
有益效果：与现有技术相比，本发明具有如下显著优点：1、具有良好的组织均匀性及纯净度；2、组织为铁素体+珠光体，贝氏体含量≤3％，钢材纯净度K3≤20，硬度≤180HBW，硬度散差≤20HBW，表面缺陷深度≤0.30mm，表面脱碳层≤0.40mm；3、具备优良的冷锻性能及使用性能。
附图说明
图1为本发明高温回火后金相组织图；
图2为本发明表面脱碳层深度图。
具体实施方式
下面结合附图对本发明的技术方案作进一步说明。
如图1、图2所示，本实施例所述的控轧加高温回火的齿轮钢棒材，包括按照重量百分比包括以下组分：C：0.15-0.25％、Mn：1.00-1.50％、Si≤0.35％、P≤0.030％、S≤0.030％、Cr：1.00-1.50％、Al：0.010-0.045％，其余为Fe和不可避免的杂质。
一种控轧加高温回火的齿轮钢棒材的制备方法，包括以下步骤：
步骤1：对齿轮钢用棒材开坯加热；步骤2：开坯除磷；步骤3：二火轧制加热；步骤4：二火轧制除磷；步骤5：终轧温度；步骤6：高温回火；步骤7：超声波探伤、漏磁探伤。
步骤1中，所述开坯加热的温度：950-1270℃，开坯加热的总加热时间≥240min。
步骤2中，所述开坯除磷采用高压水除鳞，压力≥13MPa。
步骤3中，所述二火轧制加热温度为980℃-1240℃，总加热时间≥180min。
步骤4中，所述二火轧制除磷采用高压水除鳞，压力≥13MPa。
步骤5中，所述终轧温度≤1000℃。
步骤6中，所述高温回火采用辊底式连续炉高温回火，温度为620-680℃，并设置高温段的保温时间，所述高温段保温时间≥2h。
步骤7中，所述超声波探伤精度满足GB4162的A级要求，表面缺陷深度≤0.30mm。
步骤1中使用的齿轮钢用棒材，按照重量百分比包括以下组分：
C：0.20％、Mn：1.25％、Si：0.11％、P：0.010％、S：0.005％、Cr：1.13％、Al：0.021％，其余为Fe和不可避免的杂质。
实施例1
本实施例采用规格为φ20-80mm的冷锻用的齿轮钢用棒材具体成分，如下表1(单位：％)：
表1
C Si Mn P S Cr Al H O
0.20 0.11 1.25 0.010 0.005 1.13 0.021 0.00012 0.0008
本实施例实施例按照以下工艺执行：
步骤1：开坯加热：开坯加热温度：950-1270℃，总加热时间≥240min；
步骤2：开坯除磷：采用高压水除鳞，压力≥13MPa；
步骤3：二火轧制加热：二火轧制加热温度：980℃-1240℃，总加热时间≥180min；
步骤4：二火轧制除磷：采用高压水除鳞，压力≥13MPa；
步骤5：终轧温度：终轧温度≤1000℃；
步骤6：高温回火：辊底式连续炉高温回火，高温回火温度620-680℃，高温段保温时间≥2h；
步骤7：超声波探伤、漏磁探伤：超声波探伤精度满足GB4162的A级要求，表面缺陷深度≤0.30mm。
本实施例选取实施例组织类型、纯净度、硬度、脱碳层深度如下：
组织为铁素体+珠光体，贝氏体含量≤3％，见附图1。
钢材纯净度K3：8。
高温回火后的硬度160HBW，硬度散差15HBW。
表面脱碳层0.35mm，见附图2。
由上述性能可知，本发明棒材可完全满足下游客户的冷精锻要求，客户冷锻成齿轮后，各项性能良好，完全满足使用要求。

Claims (10)

  1. 一种控轧加高温回火的齿轮钢棒材，其特征在于，按照重量百分比包括以下组分：C：0.15-0.25％、Mn：1.00-1.50％、Si≤0.35％、P≤0.030％、S≤0.030％、Cr：1.00-1.50％、Al：0.010-0.045％，其余为Fe和不可避免的杂质。
  2. 一种控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：包括以下步骤：
    步骤1：对齿轮钢用棒材开坯加热；
    步骤2：开坯除磷；
    步骤3：二火轧制加热；
    步骤4：二火轧制除磷；
    步骤5：终轧温度；
    步骤6：高温回火；
    步骤7：超声波探伤、漏磁探伤。
  3. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤1中，所述开坯加热的温度：950-1270℃，开坯加热的总加热时间≥240min。
  4. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤2中，所述开坯除磷采用高压水除鳞，压力≥13MPa。
  5. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤3中，所述二火轧制加热温度为980℃-1240℃，总加热时间≥180min。
  6. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤4中，所述二火轧制除磷采用高压水除鳞，压力≥13MPa。
  7. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤5中，所述终轧温度≤1000℃。
  8. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤6中，所述高温回火采用辊底式连续炉高温回火，温度为620-680℃，并设置高温段的保温时间，所述高温段保温时间≥2h。
  9. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤7中，所述超声波探伤精度满足GB4162的A级要求，表面缺陷深度≤0.30mm。
  10. 根据权利要求2所述控轧加高温回火的齿轮钢棒材的制备方法，其特征在于：所述步骤1中使用的齿轮钢用棒材，按照重量百分比包括以下组分：
    C：0.20％、Mn：1.25％、Si：0.11％、P：0.010％、S：0.005％、Cr：1.13％、Al：0.021％，其余为Fe和不可避免的杂质。
PCT/CN2021/096016 2021-04-29 2021-05-26 一种控轧加高温回火的齿轮钢棒材 WO2022227160A1 (zh)

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