WO2015197007A1 - Carburized alloy steel, method for preparing same, and use thereof - Google Patents

Carburized alloy steel, method for preparing same, and use thereof Download PDF

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WO2015197007A1
WO2015197007A1 PCT/CN2015/082298 CN2015082298W WO2015197007A1 WO 2015197007 A1 WO2015197007 A1 WO 2015197007A1 CN 2015082298 W CN2015082298 W CN 2015082298W WO 2015197007 A1 WO2015197007 A1 WO 2015197007A1
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alloy steel
carburized
mass percentage
steel
blank
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PCT/CN2015/082298
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French (fr)
Chinese (zh)
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文超
董雯
刘忠伟
陈亮
梁会雷
徐宁
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南车戚墅堰机车车辆工艺研究所有限公司
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Priority to CN201580032454.XA priority Critical patent/CN106661705B/en
Priority to AU2015281542A priority patent/AU2015281542B2/en
Publication of WO2015197007A1 publication Critical patent/WO2015197007A1/en

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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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

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  • the impurities in the alloy steel further include N, O and H elements, wherein the mass percentage of N is ⁇ 0.02%, the mass percentage of O is ⁇ 0.002%, and the mass percentage of H is ⁇ 0.0002%.
  • V+Nb+Al>0.30% the effect of refining the grain size is not obvious, and the coarse grain size brings about the toughness of the alloy. Unfavorable influence, when V+Nb+Al ⁇ 0.20%, the effect of refining the grain size is better, and the toughness of the alloy is the best.
  • H Harmful gas element, when it is too high, the toughness is lowered; therefore, the content of H in the alloy steel of the present invention is controlled to be ⁇ 2.0 ppm.
  • the components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.23%, Si: 0.14%, Mn: 0.45%, P: 0.008%, S: 0.004%, Cr: 0.45%, Ni: 3.05 %, Mo: 0.79%, Al: 0.02%, Nb: 0.09%, N: 0.0078%, O: 0.0012%, H: 0.00013%, the balance being iron and unavoidable impurities.
  • the components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.22%, Si: 0.08%, Mn: 0.50%, P: 0.007%, S: 0.004%, Cr: 0.76%, Ni: 3.19 %, Mo: 0.74%, Al: 0.03%, Nb: 0.08%, N: 0.0072%, O: 0.0016%, H: 0.00015%, the balance being iron and unavoidable impurities.
  • the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
  • the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
  • Normalizing and tempering the sample blank firstly raise the blank to 920 ° C, heat it for 1 h, then air-cool to normal temperature by blowing air through the blower; then warm the blank to 700 ° C, keep warm for 1 h, blow through the blower Way of air cooling to normal temperature;

Abstract

A carburized alloy steel and a method for preparing same. The elements of the alloy are present in the following mass percentages: C: 0.15%-0.25%, Si: ≤0.30%, Mn: 0.30%-1.20%, P: ≤ 0.015%, S: ≤ 0.010%, Cr: 0.30%-1.50%, Ni: 2.80%-3.80%, Mo: 0.30%-1.00%, Al: 0.01%-0.08%, and at least one of V: 0.05%-0.15% and Nb: 0.025%-0.10%, the remainder being Fe and unavoidable impurities; and the mass percentage content of V, Nb and Al satisfies V+Nb+Al≤0.30%. The carburized alloy steel is obtained by means of smelting, blank casting, normalizing/tempering treatment, and quenching/tempering treatment. The quenching treatment involves increasing the temperature of a blank to 800°C-860°C, maintaining the temperature for 0.8h-1.5h, then placing into a rapid quench oil to cool to the temperature of the rapid quench oil.

Description

渗碳合金钢及其制备方法和应用Carburizing alloy steel and preparation method and application thereof 技术领域Technical field
本发明涉及一种合金钢，尤其涉及一种至少适用于制造重载齿轮的渗碳合金钢，属于铁基合金领域。The invention relates to an alloy steel, in particular to a carburized alloy steel suitable for at least manufacturing heavy-duty gears, and belongs to the field of iron-based alloys.
背景技术Background technique
世界上可使用的渗碳钢种类比较多，但高性能的优质渗碳钢比较少。重载齿轮用渗碳钢必须具有优越的淬透性、较细的晶粒度、较小的内氧化、高疲劳性能和良好的综合力学性能。There are many types of carburized steel that can be used in the world, but high-performance high-quality carburized steel is relatively rare. Carburized steel for heavy duty gears must have superior hardenability, finer grain size, less internal oxidation, high fatigue properties and good overall mechanical properties.
目前，我国25吨及以上轴重的机车齿轮、大功率风力发电齿轮和大功率矿山机械齿轮通常采用牌号为20Cr2Ni4、18Cr2Ni4W、17Cr2Ni2Mo等高级优质渗碳钢。这些现有的重载齿轮用渗碳钢，其成分匹配不尽合理，综合力学性能不是很理想，存在诸多不足。例如：17Cr2Ni2Mo虽然具有优良的工艺性能，但是屈服强度较低，淬透性与20Cr2Ni4、18Cr2Ni4W相比较差；18Cr2Ni4W虽然具有优良的淬透性和高强度，但是工艺性能很差，且由于Ni元素的含量较高，生产成本偏高，经济性较差；20Cr2Ni4具有较好的综合性能和经济性，但是淬透性仍不令人满意，且内氧化较大。At present, China's 25-ton and above axle load locomotive gears, high-power wind power gears and high-power mining machinery gears are usually graded 20Cr2Ni4, 18Cr2Ni4W, 17Cr2Ni2Mo and other high-quality carburized steel. These existing heavy-duty gears use carburized steel, the composition of which is not reasonable, and the comprehensive mechanical properties are not ideal, and there are many deficiencies. For example, although 17Cr2Ni2Mo has excellent process performance, the yield strength is low, and the hardenability is poor compared with 20Cr2Ni4 and 18Cr2Ni4W. Although 18Cr2Ni4W has excellent hardenability and high strength, the process performance is poor, and due to the Ni element The content is high, the production cost is high, and the economy is poor; 20Cr2Ni4 has good comprehensive performance and economy, but the hardenability is still not satisfactory, and the internal oxidation is large.
中国专利文献CN1851024A(申请号：200510018605.4)公开了一种重载齿轮钢，其化学成分重量百分比为：C 0.14～0.20，Mn 1.2～1.60，Si≤0.12，P≤0.03，S 0.015～0.04，Cr 1.30～1.80，W≤0.05，Ti 0.04～0.10，O≤20ppm，余量为Fe和其他杂质。Chinese patent document CN1851024A (Application No.: 200510018605.4) discloses a heavy-duty gear steel whose chemical composition weight percentage is: C 0.14 to 0.20, Mn 1.2 to 1.60, Si ≤ 0.12, P ≤ 0.03, S 0.015 to 0.04, Cr 1.30 to 1.80, W ≤ 0.05, Ti 0.04 to 0.10, O ≤ 20 ppm, and the balance is Fe and other impurities.
中国专利文献CN101397631A(申请号：200710153141.7)公开了一种在低温下具有低变形阻力和高极限压缩率、从而冷锻性优良的、而且渗碳变形较小的表面渗碳钢；其是冷锻性和低渗碳变形特性优良的表面渗碳钢，其特征在于，含有：以质量％计，C：0.07～0.3％、Si：0.01～0.15％、Mn：0.1～0.7％、P：0.03％以下、S：0.002～0.10％、Al：0.01～0.08％、Cr：0.7～1.5％、Ti：0.01～0.15％、B：0.0005～0.005％、N：0.008％以下，余量由Fe和不可避免的杂质构成；金属组织的65％以上是铁素体相，贝氏体相为15％以下。Chinese Patent Document CN101397631A (Application No.: 200710153141.7) discloses a surface carburized steel having low deformation resistance and high ultimate compression ratio at low temperature, thereby excellent cold forgeability and small carburization deformation; A surface-carburized steel excellent in properties and low-permeability carbon deformation characteristics, comprising: C: 0.07 to 0.3%, Si: 0.01 to 0.15%, Mn: 0.1 to 0.7%, P: 0.03% by mass% Hereinafter, S: 0.002 to 0.10%, Al: 0.01 to 0.08%, Cr: 0.7 to 1.5%, Ti: 0.01 to 0.15%, B: 0.0005 to 0.005%, and N: 0.008% or less, the balance being Fe and inevitable The impurity is composed; more than 65% of the metal structure is a ferrite phase, and a bainite phase is 15% or less.
上述中国专利揭示的两种渗碳钢添加了Mn、Cr、Ti等合金，但是， Mn、Cr、Ti等合金成分在增加材料强度的同时却带来了材料塑性和韧性的明显降低。尤其是Ti元素，虽然其可以细化晶粒，提高强度，但是Ti元素的添加极易造成齿轮的疲劳寿命降低。The two kinds of carburized steels disclosed in the above Chinese patents are alloyed with Mn, Cr, Ti, etc., however, Alloy compositions such as Mn, Cr, and Ti increase the strength of the material while causing a significant decrease in material ductility and toughness. In particular, the Ti element, although it can refine the grains and increase the strength, the addition of the Ti element is liable to cause a decrease in the fatigue life of the gear.
中国专利文献CN102080188A(申请号：201010603965.1)公开了一种CrNiMo系易切削齿轮钢及其制备方法，钢的化学成分重量百分比％为：C 0.17～0.23，Si 0.15～0.37，Mn 0.60～0.95，Cr 0.35～0.65，Ni 0.35～0.75，Mo 0.15～0.25，P≤0.030，S 0.010～0.040，Al 0.005～0.050，Ca/S 0.3～0.6；余为Fe和微量杂质。制备方法，包括初炼炉(电炉或转炉)冶炼、LF+VD(或RH)炉外精炼、连铸、轧制，其特征在于，采用炉外精炼及真空脱气处理使钢中氧含量不大于15×10-6；控制微量元素S的含量，改善CrNiMo系齿轮钢的切削性能，使得该合金钢适于高速切削加工、重要精密零件。该齿轮钢Ni元素和Mo元素的含量较低，其综合力学性能较差，无法满足重载齿轮的要求。Chinese Patent Document CN102080188A (Application No.: 201010603965.1) discloses a CrNiMo-based free-cutting gear steel and a preparation method thereof, wherein the chemical composition percentage of steel is: C 0.17 to 0.23, Si 0.15 to 0.37, Mn 0.60 to 0.95, Cr 0.35 to 0.65, Ni 0.35 to 0.75, Mo 0.15 to 0.25, P ≤ 0.030, S 0.010 to 0.040, Al 0.005 to 0.050, Ca/S 0.3 to 0.6; the balance is Fe and trace impurities. The preparation method comprises the smelting of the preliminary furnace (electric furnace or converter), the LF+VD (or RH) furnace refining, continuous casting and rolling, and is characterized in that the oxygen content in the steel is not determined by the external refining and the vacuum degassing treatment. It is larger than 15×10 -6 ; it controls the content of trace element S and improves the cutting performance of CrNiMo gear steel, making it suitable for high-speed machining and important precision parts. The content of Ni element and Mo element in the gear steel is low, and its comprehensive mechanical properties are poor, which cannot meet the requirements of heavy-duty gears.
因此，为满足25吨及以上轴重的机车齿轮、大功率风力发电齿轮和大功率矿山机械齿轮等重载齿轮的性能要求，开发一种高性能的渗碳合金钢显得尤为迫切。Therefore, in order to meet the performance requirements of heavy-duty gears such as locomotive gears, high-power wind power gears and high-power mining machinery gears with axle loads of 25 tons and above, it is particularly urgent to develop a high-performance carburized alloy steel.
发明内容Summary of the invention
本发明的目的之一在于，优化渗碳合金钢在淬透性、屈强比、内氧化和抗高温晶粒长大等方面的特性。One of the objects of the present invention is to optimize the properties of carburized alloy steel in terms of hardenability, yield ratio, internal oxidation, and high temperature grain growth resistance.
本发明的还一目的在于，提高渗碳合金钢的抗疲劳性能和综合力学性能。Still another object of the present invention is to improve the fatigue resistance and overall mechanical properties of carburized alloy steel.
为实现以上目的或者其他目的，本发明提供以下技术方案：To achieve the above or other objects, the present invention provides the following technical solutions:
按照本发明的一方面，提供一种渗碳合金钢，该合金钢的组分及其质量百分比为C：0.15％～0.25％，Si：≤0.30％，Mn：0.30％～1.20％，Cr：0.30％～1.50％，Ni：2.80％～3.80％，Mo：0.30％～1.00％，Al：0.01％～0.08％，以及V和Nb中的至少一种，余量为铁和不可避免的杂质；且当所述合金钢包含V时，V的质量百分比为0.05％～0.15％，当上述合金钢包含Nb时，Nb的质量百分比为0.025％～0.10％，并且所述V、Nb和Al的质量百分比含量符合V+Nb+Al≤0.30％。According to an aspect of the invention, there is provided a carburized alloy steel having a composition and a mass percentage of C: 0.15% to 0.25%, Si: ≤ 0.30%, Mn: 0.30% to 1.20%, Cr: 0.30% to 1.50%, Ni: 2.80% to 3.80%, Mo: 0.30% to 1.00%, Al: 0.01% to 0.08%, and at least one of V and Nb, the balance being iron and unavoidable impurities; And when the alloy steel contains V, the mass percentage of V is 0.05% to 0.15%, and when the above alloy steel contains Nb, the mass percentage of Nb is 0.025% to 0.10%, and the mass of the V, Nb and Al The percentage content is in accordance with V+Nb+Al≤0.30%.
进一步，上述所述合金钢中的Al的质量百分比含量可以为0.02％～0.05％；所述V、Nb和Al的质量百分比含量符合 V+Nb+Al≤0.20％。Further, the mass percentage of Al in the alloy steel described above may be 0.02% to 0.05%; the mass percentage content of the V, Nb and Al is in accordance with V+Nb+Al≤0.20%.
进一步，上述合金钢中的C的质量百分比含量为0.15％～0.23％，Si的质量百分比含量为≤0.25％。Further, the mass percentage of C in the above alloy steel is 0.15% to 0.23%, and the mass percentage content of Si is ≤0.25%.
进一步，上述合金钢中的Mn的质量百分比含量为0.40％～1.00％，Cr的质量百分比含量为0.40％～1.20％。Further, the mass percentage of Mn in the above alloy steel is 0.40% to 1.00%, and the mass percentage of Cr is 0.40% to 1.20%.
进一步，上述合金钢中的Ni的质量百分比含量为3.00％～3.80％，Mo的质量百分比含量为0.40％～0.80％。Further, the mass percentage of Ni in the above alloy steel is 3.00% to 3.80%, and the mass percentage of Mo is 0.40% to 0.80%.
进一步，上述合金钢中的杂质包括P和S元素，其中P的质量百分比含量为≤0.015％，S的质量百分比含量为≤0.010％。Further, the impurities in the above alloy steel include P and S elements, wherein the mass percentage content of P is ≤0.015%, and the mass percentage content of S is ≤0.010%.
进一步，所述合金钢中的杂质还包括N、O和H元素，其中N的质量百分比含量≤0.02％，O的质量百分比含量≤0.002％，H的质量百分比含量≤0.0002％。Further, the impurities in the alloy steel further include N, O and H elements, wherein the mass percentage of N is ≤ 0.02%, the mass percentage of O is ≤ 0.002%, and the mass percentage of H is ≤ 0.0002%.
上述N的质量百分比含量优选≤0.01％。The mass percentage content of the above N is preferably ≤0.01%.
按照本发明的又一方面，提供一种上述渗碳合金钢的制备方法，包括以下步骤：According to still another aspect of the present invention, a method for preparing the above carburized alloy steel is provided, comprising the steps of:
A.根据合金钢的组分和含量进行配料，采用现有的冶炼和精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by the existing smelting and refining process;
B.浇注钢锭，将钢锭轧制成毛坯；B. pouring a steel ingot to roll the steel ingot into a blank;
C.正火回火处理；和C. normalizing tempering; and
D.淬火回火处理，其中，所述淬火回火处理是将毛坯升温至800℃～860℃，保温0.8h～1.5h后，放入快速淬火油中冷却至快速淬火油的使用温度，然后取出毛坯再进行回火处理。D. quenching and tempering treatment, wherein the quenching and tempering treatment is to raise the temperature of the blank to 800 ° C ~ 860 ° C, after the temperature of 0.8 h ~ 1.5 h, put into the rapid quenching oil to cool to the use temperature of the rapid quenching oil, and then The blank is taken out and tempered.
进一步，上述正火回火处理是将毛坯升温至900℃～960℃，保温0.8h～1.5h后，风冷至室温，再将所述毛坯升温至630℃～750℃，保温0.8h～1.5h后，风冷至室温。Further, the normalizing and tempering treatment is to raise the temperature of the blank to 900 ° C to 960 ° C, heat the temperature for 0.8 h to 1.5 h, and then air-cool to room temperature, and then raise the blank to 630 ° C to 750 ° C, and keep warm for 0.8 h to 1.5. After h, air cool to room temperature.
进一步，上述淬火回火处理中，在回火时将毛坯升温至160℃～220℃，保温2.5h～3.5h后，风冷至室温。Further, in the above quenching and tempering treatment, the billet is heated to 160 ° C to 220 ° C during tempering, and after being kept for 2.5 h to 3.5 h, it is air-cooled to room temperature.
进一步，上述步骤A中，所述冶炼和精炼工艺采用电炉进行冶炼和采用钢包精炼炉+真空脱气炉进行精炼的工艺。Further, in the above step A, the smelting and refining process uses an electric furnace for smelting and a refining process using a ladle refining furnace + a vacuum degassing furnace.
进一步，上述步骤D中，所述快速淬火油的使用温度为40℃～100℃。Further, in the above step D, the quick quenching oil is used at a temperature of 40 ° C to 100 ° C.
按照本发明的还一方面，上述渗碳合金钢的应用是用于制造重载 齿轮。According to still another aspect of the present invention, the above carburized alloy steel is used for manufacturing heavy loads gear.
下面对本发明实施例的渗碳合金钢中所含元素在合金中所起的作用，以及其优选的含量(质量百分比范围)做详细的描述：The role of the elements contained in the carburized alloy steel of the embodiment of the present invention in the alloy, and its preferred content (range of mass percentage) are described in detail below:
C：主要的固溶强化元素；为了保证具有足够的强度，C必须在0.15％以上，但C含量超过0.25％时，会使得强度超高，且韧性严重下降，因此，本发明合金钢中的C含量控制在0.15％～0.25％，进一步的优选为0.15％～0.23％。C: the main solid solution strengthening element; in order to ensure sufficient strength, C must be above 0.15%, but when the C content exceeds 0.25%, the strength is extremely high, and the toughness is seriously degraded, therefore, in the alloy steel of the present invention The C content is controlled to be 0.15% to 0.25%, and more preferably 0.15% to 0.23%.
Si：脱氧剂；为了提高抗内氧化能力，本发明合金钢中的Si含量控制在0.30％以下，为了保证脱氧效果和一定的屈服强度，进一步优选为0.25％以下。Si: a deoxidizer; in order to improve the resistance to internal oxidation, the Si content in the alloy steel of the present invention is controlled to 0.30% or less, and more preferably 0.25% or less in order to secure the deoxidation effect and a certain yield strength.
Mn：良好的脱氧剂和脱硫剂，同时也提高钢的淬透性、改善钢的热加工性能；但是，过高的Mn含量会降低渗层韧性，因此，本发明合金钢中的Mn含量控制在0.30％～1.20％；进一步优选为0.40％～1.00％。Mn: good deoxidizer and desulfurizer, but also improve the hardenability of steel and improve the hot workability of steel; however, too high Mn content will reduce the toughness of the layer, therefore, the control of Mn content in the alloy steel of the invention It is 0.30% to 1.20%; more preferably 0.40% to 1.00%.
P：在钢液凝固过程中易形成微观偏析，随后在奥氏体化过程中偏聚到晶界，使得钢脆性显著增加；因此，本发明合金钢中的P含量控制在0.015％以下。P: Microsegregation is easily formed during solidification of the molten steel, and then segregated to the grain boundary during austenitizing, so that the brittleness of the steel is remarkably increased; therefore, the P content in the alloy steel of the present invention is controlled to be less than 0.015%.
S：不可避免的杂质元素，其与Mn形成MnS夹杂物在晶界偏析时会降低钢的韧性；因此，本发明合金钢中的S含量控制在0.010％以下。S: an unavoidable impurity element which reduces the toughness of the steel when the MnS inclusions are segregated at the grain boundary with the Mn; therefore, the S content in the alloy steel of the present invention is controlled to be 0.010% or less.
Cr：主要淬透性元素，提高钢的强度、硬度和耐磨性；但是，过高的Cr含量会降低钢的冷加工性能，因此，本发明合金钢中的Cr含量控制在0.30％～1.50％；进一步优选为0.40％～1.20％。Cr: Main hardenability element, which improves the strength, hardness and wear resistance of steel; however, too high Cr content will reduce the cold workability of steel. Therefore, the Cr content in the alloy steel of the present invention is controlled at 0.30% to 1.50%. More preferably, it is 0.40% - 1.20%.
Ni：主要的固溶强化元素，随着Ni含量的增加，钢的常温强度也会增加，并且Ni的添加对合金的塑性和韧性影响不大；但是过高的Ni会降低钢的热加工性能，且成本过高，因此，本发明合金钢中的Ni含量控制在2.80％～3.80％；进一步优选为3.00％～3.80％。Ni: The main solid solution strengthening element, with the increase of Ni content, the room temperature strength of steel will also increase, and the addition of Ni has little effect on the plasticity and toughness of the alloy; but too high Ni will reduce the hot workability of steel. Further, the cost is too high. Therefore, the Ni content in the alloy steel of the present invention is controlled to 2.80% to 3.80%, and more preferably 3.00% to 3.80%.
Mo：主要的淬透性元素，能同时提高基体和渗层的淬透性；但是过量的Mo会造成锻造性能下降，且成本过高，因此，本发明合金钢中的Mo含量控制在0.30％～1.00％；进一步优选为0.40％～0.80％。Mo: The main hardenability element can simultaneously improve the hardenability of the matrix and the layer; however, excessive Mo causes the forging property to decrease and the cost is too high. Therefore, the Mo content in the alloy steel of the present invention is controlled at 0.30%. ～1.00%; more preferably 0.40% to 0.80%.
Al、Nb、V：Al是脱氧剂和细化晶粒元素；Al含量在0.01％以下时，细化晶粒作用不明显，但Al含量在0.08％以上时，其脱氧作用增加也不明显，且易形成较大的夹杂物，影响疲劳性能，因此，本发明合金钢中的Al含量控制在0.01％～0.08％；进一步优选为0.02％～ 0.05％。Nb是细化晶粒元素，Nb含量在0.025％以下时，细化晶粒作用不明显，Nb含量在0.10％以上时，细化晶粒作用达到饱和，增幅也不明显；因此，本发明合金钢中的Nb含量控制在0.025％～0.10％。V是细化晶粒元素，V含量在0.05％以下，细化晶粒作用不明显，V含量在0.15％以上时，细化晶粒作用达到饱和，增幅也不明显，因此，本发明合金钢中的V含量控制在0.05％～0.15％。同时，本发明合金钢中Al、V、Nb复合添加时，则必须符合V+Nb+Al≤0.30％，进一步优化为V+Nb+Al≤0.20％，这是由于合理控制Al、V、Nb的复合添加量可以通过细化晶粒度从而间接影响合金的韧性，当V+Nb+Al>0.30％时，细化晶粒度的效果不明显，晶粒度粗大会对合金的韧性带来不利的影响，当V+Nb+Al≤0.20％，细化晶粒度的效果较好，合金韧性最佳。Al, Nb, V: Al is a deoxidizer and refined grain elements; when the Al content is below 0.01%, the effect of refining grains is not obvious, but when the Al content is above 0.08%, the deoxidation is not obvious. Moreover, it is easy to form large inclusions and affect fatigue performance. Therefore, the Al content in the alloy steel of the present invention is controlled to be 0.01% to 0.08%; further preferably 0.02% to ～ 0.05%. Nb is refined grain element. When the Nb content is below 0.025%, the grain refining effect is not obvious. When the Nb content is above 0.10%, the grain refining effect is saturated and the increase is not obvious. Therefore, the alloy of the present invention is not obvious. The Nb content in the steel is controlled to be 0.025% to 0.10%. V is refined grain element, the V content is below 0.05%, the grain refining effect is not obvious, and when the V content is above 0.15%, the grain refining effect is saturated, and the increase is not obvious. Therefore, the alloy steel of the invention The V content in the control is controlled to be 0.05% to 0.15%. At the same time, when Al, V and Nb are added in the alloy steel of the invention, it must conform to V+Nb+Al≤0.30%, and further optimized to V+Nb+Al≤0.20%, which is due to reasonable control of Al, V, Nb. The composite addition amount can indirectly affect the toughness of the alloy by refining the grain size. When V+Nb+Al>0.30%, the effect of refining the grain size is not obvious, and the coarse grain size brings about the toughness of the alloy. Unfavorable influence, when V+Nb+Al≤0.20%, the effect of refining the grain size is better, and the toughness of the alloy is the best.
N：冶炼不可避免的气体元素，能与Al、Nb、V等结合形成化合物，从而细化晶粒；但过高会偏聚晶界而降低晶界强度，因此，本发明合金钢中的N的含量控制在≤0.02％，进一步优选为≤0.01％。N: An inevitable gas element in smelting, which can combine with Al, Nb, V, etc. to form a compound to refine grains; but too high, it will segregate grain boundaries and reduce grain boundary strength. Therefore, N in the alloy steel of the present invention The content is controlled to be ≤0.02%, and more preferably ≤0.01%.
O：有害气体元素，过高时会降低疲劳性能；因此，本发明合金钢中的O的含量控制在≤20ppm。O: Harmful gas element, when it is too high, the fatigue property is lowered; therefore, the content of O in the alloy steel of the present invention is controlled to be ≤ 20 ppm.
H：有害气体元素，过高时会降低韧性；因此，本发明合金钢中的H的含量控制在≤2.0ppm。H: Harmful gas element, when it is too high, the toughness is lowered; therefore, the content of H in the alloy steel of the present invention is controlled to be ≤ 2.0 ppm.
本发明具有积极的效果：The invention has positive effects:
(1)本发明的渗碳合金钢通过Mn、Cr、Ni、Mo元素及其与C的合理配比，在保证材料钢强度增加的同时，还能保证材料的塑性和韧性不受较大影响，避免了因强度增加导致材料塑性和韧性明显下降的现象。所制得的渗碳合金钢材料综合力学性能优良；明显克服了现有技术中的渗碳合金钢由于各成分匹配不尽合理而导致在强度和塑、韧性方面不能兼顾的矛盾。另外，还有效地提高了渗碳合金钢的淬透性，从而使得该钢材可适用于大模数齿轮。(1) The carburized alloy steel of the present invention passes through the Mn, Cr, Ni, Mo elements and its reasonable ratio with C, and ensures the strength of the material steel while ensuring that the plasticity and toughness of the material are not greatly affected. This avoids the phenomenon that the plasticity and toughness of the material decrease significantly due to the increase in strength. The obtained carburized alloy steel material has excellent comprehensive mechanical properties; obviously overcomes the contradiction between the strength, the plasticity and the toughness of the carburized alloy steel in the prior art due to the unreasonable matching of the components. In addition, the hardenability of the carburized alloy steel is effectively improved, so that the steel can be applied to a large modulus gear.
(2)本发明的渗碳合金钢通过Al、V、Nb元素的添加或者复合添加，使得合金在成型过程中具有优异的抗晶粒长大性能，尤其适用于高温渗碳的零件。(2) The carburized alloy steel of the present invention is added or compositely added by Al, V, Nb elements, so that the alloy has excellent resistance to grain growth during the molding process, and is particularly suitable for high temperature carburized parts.
(3)本发明的渗碳合金钢通过Si、Ni和Mo元素的优化配合，可以降低晶界在渗碳过程中的内氧化，并使得其在较长的渗碳时间中，其内部氧化特征比传统钢有较低的内氧化深度值，尤其适用于对内氧 化有非常高要求的机械零件。(3) The carburized alloy steel of the present invention can reduce the internal oxidation of the grain boundary during the carburizing process by the optimized combination of Si, Ni and Mo elements, and the internal oxidation characteristics of the grain boundary during the long carburizing time. Lower internal oxidation depth than conventional steel, especially suitable for internal oxygen Mechanical parts with very high requirements.
(4)本发明的渗碳合金钢通过Cr、Ni、Mo元素的合理选择及其配比，使得该钢材制造容易、加工工艺性能优良，且生产成本相对较低，有利于提高经济效益。(4) The carburized alloy steel of the invention has a reasonable selection of Cr, Ni and Mo elements and a ratio thereof, so that the steel is easy to manufacture, the processing performance is excellent, and the production cost is relatively low, which is beneficial to improving economic benefits.
(5)本发明的渗碳合金钢具有极小的内氧化、高淬透性、高屈强比和抗高温晶粒长大特性，特别适用于制造对抗疲劳性能和综合力学性能有非常高要求的机械零件，如重载齿轮等。(5) The carburized alloy steel of the invention has extremely small internal oxidation, high hardenability, high yield ratio and high temperature grain growth resistance, and is particularly suitable for manufacturing fatigue resistance and comprehensive mechanical properties. Mechanical parts, such as heavy-duty gears.
附图说明DRAWINGS
图1是本发明实施例1的渗碳合金钢与20Cr2Ni4、18Cr2Ni4W和17Cr2Ni2Mo的渗碳合金钢的淬透性对比关系图。BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a graph showing the comparison of the hardenability of a carburized alloy steel of Example 1 of the present invention with carburized alloy steels of 20Cr2Ni4, 18Cr2Ni4W and 17Cr2Ni2Mo.
图2是本发明实施例1至实施例7的渗碳合金钢的淬透性对比关系图。Fig. 2 is a graph showing the comparison of hardenability of carburized alloy steels of Examples 1 to 7 of the present invention.
图3是对比例1的17Cr2Ni2Mo的渗碳合金钢的内部氧化深度与渗碳层深度的关系图，图中给出了3个试样的情况。Fig. 3 is a graph showing the relationship between the internal oxidation depth of the carburized alloy steel of 17Cr2Ni2Mo of Comparative Example 1 and the depth of the carburized layer, and the case of three samples is shown.
图4是本发明实施例1的渗碳合金钢的内部氧化深度与渗碳层深度的关系图，图中给出了实施例1的3个试样的情况。其中，在渗碳深度约0.5毫米处，试样编号2的氧化深度的数值与试样编号3的氧化深度的数值基本重叠，均约为0.002毫米；在渗碳深度约1.25毫米处，试样编号1的氧化深度的数值与试样编号2的氧化深度的数值基本重叠，均约为0.002毫米；在渗碳深度约1.8毫米处，试样编号1的氧化深度的数值与试样编号3的氧化深度的数值基本重叠，均约为0.002毫米；在渗碳深度约2.5毫米处，试样编号2的氧化深度的数值与试样编号3的氧化深度的数值基本重叠，均约为0.002毫米；在渗碳深度约3.25毫米处，试样编号2的氧化深度的数值与试样编号3的氧化深度的数值基本重叠，均约为0.002毫米。Fig. 4 is a graph showing the relationship between the internal oxidation depth of the carburized alloy steel and the depth of the carburized layer in Example 1 of the present invention, and shows the case of the three samples of Example 1. Wherein, at a carburization depth of about 0.5 mm, the value of the oxidation depth of sample No. 2 substantially overlaps with the value of the oxidation depth of sample No. 3, both being about 0.002 mm; at a carburization depth of about 1.25 mm, the sample The value of the oxidation depth of No. 1 substantially overlaps with the value of the oxidation depth of sample No. 2, both being about 0.002 mm; at the carburization depth of about 1.8 mm, the value of the oxidation depth of sample No. 1 and the sample No. 3 The values of the oxidation depths are substantially overlapped, both being about 0.002 mm; at a carburization depth of about 2.5 mm, the value of the oxidation depth of sample No. 2 substantially overlaps with the value of the oxidation depth of sample No. 3, both being about 0.002 mm; At a carburization depth of about 3.25 mm, the value of the oxidation depth of sample No. 2 substantially overlaps with the value of the oxidation depth of sample No. 3, both being about 0.002 mm.
图5是本发明实施例1至实施例7的渗碳合金钢的内部氧化深度与渗碳层深度的关系图和数据表格。Fig. 5 is a graph showing the relationship between the internal oxidation depth of the carburized alloy steels of Examples 1 to 7 of the present invention and the depth of the carburized layer, and a data table.
图6是本发明实施例1的渗碳合金钢的晶粒度与加热温度的关系图。Fig. 6 is a graph showing the relationship between the grain size of the carburized alloy steel and the heating temperature in Example 1 of the present invention.
具体实施方式 detailed description
下面具体说明上述渗碳合金钢及其制备方法的实施例，这些实施例实质用于说明本发明而非用于限定本发明的范围。The above-described examples of the carburized alloy steel and the preparation method thereof are specifically described below, and the examples are intended to be illustrative of the invention and are not intended to limit the scope of the invention.
实施例1Example 1
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.18％，Si：0.16％，Mn：0.69％，P：0.009％，S：0.005％，Cr：1.00％，Ni：3.55％，Mo：0.62％，Al：0.04％，V：0.05％，Nb：0.03％，N：0.0092％，O：0.0019％，H：0.00015％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.18%, Si: 0.16%, Mn: 0.69%, P: 0.009%, S: 0.005%, Cr: 1.00%, Ni: 3.55 %, Mo: 0.62%, Al: 0.04%, V: 0.05%, Nb: 0.03%, N: 0.0092%, O: 0.0019%, H: 0.00015%, the balance being iron and unavoidable impurities.
本实施例1的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the first embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料,采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998《钢及钢产品力学性能试验取样位置及试样制备》取试样毛坯；B. Casting steel ingots, rolling steel ingots into round steel, taking sample blanks on round steel according to national standard GB/T2975-1998 "Sampling position and sample preparation of mechanical properties of steel and steel products";
C.对试样毛坯进行正火回火处理：先将毛坯升温至950℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至750℃，保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 950 ° C, heat it for 1 h, then air-cool to room temperature by blower blowing; then warm the blank to 750 ° C, keep warm for 1 h, blow by blower Way of air cooling to room temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至860℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至220℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 860 ° C, heat it for 1 h, then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; Then take out the blank, then raise the blank to 220 ° C, keep warm for 3h, and then air-cool to room temperature by blower.
实施例2Example 2
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.15％，Si：0.20％，Mn：0.95％，P：0.008％，S：0.006％，Cr：1.20％，Ni：3.75％，Mo：0.41％，Al：0.08％，V：0.12％，N：0.0080％，O：0.0016％，H：0.00016％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.15%, Si: 0.20%, Mn: 0.95%, P: 0.008%, S: 0.006%, Cr: 1.20%, Ni: 3.75 %, Mo: 0.41%, Al: 0.08%, V: 0.12%, N: 0.0080%, O: 0.0016%, H: 0.00016%, the balance being iron and unavoidable impurities.
本实施例2的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the second embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料,采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998取试样毛坯；B. pouring steel ingot, rolling the steel ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975-1998;
C.对试样毛坯进行正火回火处理：先将毛坯升温至900℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至630℃， 保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 900 ° C, heat it for 1 h, then air-cool to room temperature by blowing air through a blower; then raise the blank to 630 ° C, After 1 h of heat preservation, air-cooled to room temperature by blowing air through a blower;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至800℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至160℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 800 ° C, heat it for 1 h, then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; Then take out the blank, then raise the blank to 160 ° C, keep warm for 3h, then air-cooled to room temperature by air blower.
实施例3Example 3
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.23％，Si：0.14％，Mn：0.45％，P：0.008％，S：0.004％，Cr：0.45％，Ni：3.05％，Mo：0.79％，Al：0.02％，Nb：0.09％，N：0.0078％，O：0.0012％，H：0.00013％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.23%, Si: 0.14%, Mn: 0.45%, P: 0.008%, S: 0.004%, Cr: 0.45%, Ni: 3.05 %, Mo: 0.79%, Al: 0.02%, Nb: 0.09%, N: 0.0078%, O: 0.0012%, H: 0.00013%, the balance being iron and unavoidable impurities.
本实施例3的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the third embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料，采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998取试样毛坯；B. pouring steel ingot, rolling the steel ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975-1998;
C.对试样毛坯进行正火回火处理：先将毛坯升温至920℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至700℃，保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 920 ° C, heat it for 1 h, then air-cool to room temperature by blowing air with a blower; then warm the blank to 700 ° C, keep warm for 1 h, blow by blower Way of air cooling to room temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至840℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至200℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 840 ° C, heat it for 1 h, and then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; Then take out the blank, then raise the blank to 200 ° C, keep warm for 3h, then air-cooled to room temperature by air blower.
实施例4Example 4
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.20％，Si：0.05％，Mn：0.50％，P：0.007％，S：0.005％，Cr：0.85％，Ni：3.30％，Mo：0.50％，Al：0.02％，V：0.10％，Nb：0.07％，N：0.0089％，O：0.0018％，H：0.00015％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.20%, Si: 0.05%, Mn: 0.50%, P: 0.007%, S: 0.005%, Cr: 0.85%, Ni: 3.30 %, Mo: 0.50%, Al: 0.02%, V: 0.10%, Nb: 0.07%, N: 0.0089%, O: 0.0018%, H: 0.00015%, the balance being iron and unavoidable impurities.
本实施例4的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the fourth embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料,采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼。A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace.
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998取试样毛坯； B. pouring steel ingot, rolling the steel ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975-1998;
C.对试样毛坯进行正火回火处理：先将毛坯升温至930℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至680℃，保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 930 ° C, heat it for 1 h, then air-cool to room temperature by air blower; then warm the blank to 680 ° C, keep warm for 1 h, blow by blower Way of air cooling to room temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至820℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至180℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 820 ° C, heat it for 1 h, then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; then the blank was taken out, and the blank was heated to 180 ° C, and after 3 hours of heat preservation, it was air-cooled to room temperature by a blower.
实施例5Example 5
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.17％，Si：0.06％，Mn：0.73％，P：0.006％，S：0.005％，Cr：1.15％，Ni：3.52％，Mo：0.65％，Al：0.02％，V：0.11％，N：0.0065％，O：0.0015％，H：0.00012％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.17%, Si: 0.06%, Mn: 0.73%, P: 0.006%, S: 0.005%, Cr: 1.15%, Ni: 3.52 %, Mo: 0.65%, Al: 0.02%, V: 0.11%, N: 0.0065%, O: 0.0015%, H: 0.00012%, the balance being iron and unavoidable impurities.
本实施例的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料,采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998取试样毛坯；B. pouring steel ingot, rolling the steel ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975-1998;
C.对试样毛坯进行正火回火处理：先将毛坯升温至930℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至680℃，保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 930 ° C, heat it for 1 h, then air-cool to room temperature by air blower; then warm the blank to 680 ° C, keep warm for 1 h, blow by blower Way of air cooling to room temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至820℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至180℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 820 ° C, heat it for 1 h, then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; then the blank was taken out, and the blank was heated to 180 ° C, and after 3 hours of heat preservation, it was air-cooled to room temperature by a blower.
实施例6Example 6
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.22％，Si：0.08％，Mn：0.50％，P：0.007％，S：0.004％，Cr：0.76％，Ni：3.19％，Mo：0.74％，Al：0.03％，Nb：0.08％，N：0.0072％，O：0.0016％，H：0.00015％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.22%, Si: 0.08%, Mn: 0.50%, P: 0.007%, S: 0.004%, Cr: 0.76%, Ni: 3.19 %, Mo: 0.74%, Al: 0.03%, Nb: 0.08%, N: 0.0072%, O: 0.0016%, H: 0.00015%, the balance being iron and unavoidable impurities.
本实施例的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料,采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼； A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998取试样毛坯；B. pouring steel ingot, rolling the steel ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975-1998;
C.对试样毛坯进行正火回火处理：先将毛坯升温至930℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至680℃，保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 930 ° C, heat it for 1 h, then air-cool to room temperature by air blower; then warm the blank to 680 ° C, keep warm for 1 h, blow by blower Way of air cooling to room temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至820℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至180℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 820 ° C, heat it for 1 h, then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; then the blank was taken out, and the blank was heated to 180 ° C, and after 3 hours of heat preservation, it was air-cooled to room temperature by a blower.
实施例7Example 7
本实施例的渗碳合金钢的组分及其质量百分比为：C：0.21％，Si：0.25％，Mn：0.49％，P：0.008％，S：0.004％，Cr：0.53％，Ni：3.25％，Mo：0.66％，Al：0.05％，V：0.09％，Nb：0.05％，N：0.0069％，O：0.0014％，H：0.00014％，余量为铁和不可避免的杂质。The components of the carburized alloy steel of the present embodiment and the mass percentage thereof are: C: 0.21%, Si: 0.25%, Mn: 0.49%, P: 0.008%, S: 0.004%, Cr: 0.53%, Ni: 3.25 %, Mo: 0.66%, Al: 0.05%, V: 0.09%, Nb: 0.05%, N: 0.0069%, O: 0.0014%, H: 0.00014%, the balance being iron and unavoidable impurities.
本实施例的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the embodiment includes the following specific steps:
A.根据合金钢的组分和含量进行配料,采用常规的电炉+钢包精炼炉(LF)+真空脱气炉的炼钢精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by a steelmaking refining process of a conventional electric furnace + ladle refining furnace (LF) + vacuum degassing furnace;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975-1998取试样毛坯；B. pouring steel ingot, rolling the steel ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975-1998;
C.对试样毛坯进行正火回火处理：先将毛坯升温至930℃，保温1h后，通过鼓风机吹风的方式风冷至室温；然后将毛坯升温至680℃，保温1h后，通过鼓风机吹风的方式风冷至室温；C. Normalizing and tempering the sample blank: firstly raise the blank to 930 ° C, heat it for 1 h, then air-cool to room temperature by air blower; then warm the blank to 680 ° C, keep warm for 1 h, blow by blower Way of air cooling to room temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至820℃，保温1h后，放入快速淬火油中冷却至快速淬火油的使用温度，快速淬火油的使用温度控制在60±5℃；然后取出毛坯，再将毛坯升温至180℃，保温3h后，通过鼓风机吹风的方式风冷至室温。D. Quenching and tempering the sample blank: firstly raise the blank to 820 ° C, heat it for 1 h, then put it into the rapid quenching oil to cool to the use temperature of the quenching oil. The use temperature of the quenching oil is controlled at 60±5. °C; then the blank was taken out, and the blank was heated to 180 ° C, and after 3 hours of heat preservation, it was air-cooled to room temperature by a blower.
对比例1Comparative example 1
本对比例选用牌号为17Cr2Ni2Mo的渗碳合金钢，合金的化学成分如表1所示。The comparative example was selected from carburized alloy steel of the grade 17Cr2Ni2Mo. The chemical composition of the alloy is shown in Table 1.
对比例1的渗碳合金的制备方法，包括以下具体步骤：The preparation method of the carburized alloy of Comparative Example 1 comprises the following specific steps:
A.根据合金的组分和含量进行配料,采用常规的钢包精炼炉+真空吹氧脱碳炉+真空脱气炉的炼钢精炼工艺进行合金熔炼； A. According to the composition and content of the alloy, the alloy is smelted by a conventional steel ladle refining furnace + vacuum oxygen decarburization furnace + vacuum degassing furnace steelmaking refining process;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975《钢及钢产品力学性能试验取样位置及试样制备》取试样毛坯；B. pouring steel ingot, rolling the ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975 "Sampling position and sample preparation of mechanical properties test of steel and steel products";
C.对试样毛坯进行正火回火处理：先将毛坯升温至920℃，保温1h后，通过鼓风机吹风的方式风冷至常温；然后将毛坯升温至700℃，保温1h后，通过鼓风机吹风的方式风冷至常温；C. Normalizing and tempering the sample blank: firstly raise the blank to 920 ° C, heat it for 1 h, then air-cool to normal temperature by blowing air through the blower; then warm the blank to 700 ° C, keep warm for 1 h, blow through the blower Way of air cooling to normal temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至840℃，保温1h后，快速淬火油冷至油温；然后将毛坯升温至200℃，保温3h后，通过鼓风机吹风的方式风冷至常温。D. Quenching and tempering of the sample blank: firstly raise the blank to 840 ° C, after 1 h of heat preservation, quench the oil to cool to oil temperature; then warm the blank to 200 ° C, keep warm for 3 h, then blow by the blower Cold to normal temperature.
对比例2Comparative example 2
本对比例选用牌号为20Cr2Ni4的渗碳合金钢，合金的化学成分如表1所示。For the comparison, the carburized alloy steel with the grade of 20Cr2Ni4 is used. The chemical composition of the alloy is shown in Table 1.
对比例2的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of Comparative Example 2 comprises the following specific steps:
A.根据合金的组分和含量进行配料,采用常规的钢包精炼炉+真空吹氧脱碳炉+真空脱气炉的炼钢精炼工艺进行合金熔炼；A. According to the composition and content of the alloy, the alloy is smelted by a conventional steel ladle refining furnace + vacuum oxygen decarburization furnace + vacuum degassing furnace steelmaking refining process;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975《钢及钢产品力学性能试验取样位置及试样制备》取试样毛坯；B. pouring steel ingot, rolling the ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975 "Sampling position and sample preparation of mechanical properties test of steel and steel products";
C.对试样毛坯进行正火回火处理：先将毛坯升温至930℃，保温1h后，通过鼓风机吹风的方式风冷至常温；然后将毛坯升温至680℃，保温1h后，通过鼓风机吹风的方式风冷至常温；C. Normalizing and tempering the sample blank: firstly raise the blank to 930 ° C, heat it for 1 h, then air-cool to normal temperature by blowing air by blower; then warm the blank to 680 ° C, keep warm for 1 h, blow by blower Way of air cooling to normal temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至820℃，保温1h后，快速淬火油冷至油温；然后将毛坯升温至180℃，保温3h后，通过鼓风机吹风的方式风冷至常温。D. Quenching and tempering the sample blank: firstly raise the blank to 820 ° C, after 1 h of heat preservation, quickly quench the oil to oil temperature; then heat the blank to 180 ° C, keep warm for 3 h, then blow by the blower Cold to normal temperature.
对比例3Comparative example 3
本对比例选用牌号为18Cr2Ni4W的渗碳合金钢，合金的化学成分如表1所示。The comparative example was selected from carburized alloy steel of 18Cr2Ni4W. The chemical composition of the alloy is shown in Table 1.
比例3的渗碳合金钢的制备方法，包括以下具体步骤：The preparation method of the carburized alloy steel of the proportion 3 comprises the following specific steps:
A.根据合金的组分和含量进行配料,采用常规的钢包精炼炉+真空吹氧脱碳炉+真空脱气炉的炼钢精炼工艺进行合金熔炼； A. According to the composition and content of the alloy, the alloy is smelted by a conventional steel ladle refining furnace + vacuum oxygen decarburization furnace + vacuum degassing furnace steelmaking refining process;
B.浇注钢锭，将钢锭轧制成圆钢，在圆钢上按照国家标准GB/T2975《钢及钢产品力学性能试验取样位置及试样制备》取试样毛坯；B. pouring steel ingot, rolling the ingot into round steel, taking the sample blank on the round steel according to the national standard GB/T2975 "Sampling position and sample preparation of mechanical properties test of steel and steel products";
C.对试样毛坯进行正火回火处理：先将毛坯升温至930℃，保温1h后，通过鼓风机吹风的方式风冷至常温；然后将毛坯升温至680℃，保温1h后，通过鼓风机吹风的方式风冷至常温；C. Normalizing and tempering the sample blank: firstly raise the blank to 930 ° C, heat it for 1 h, then air-cool to normal temperature by blowing air by blower; then warm the blank to 680 ° C, keep warm for 1 h, blow by blower Way of air cooling to normal temperature;
D.对试样毛坯进行淬火回火处理：先将毛坯升温至820℃，保温1h后，快速淬火油冷至油温；然后将毛坯升温至180℃，保温3h后，通过鼓风机吹风的方式风冷至常温。D. Quenching and tempering the sample blank: firstly raise the blank to 820 ° C, after 1 h of heat preservation, quickly quench the oil to oil temperature; then heat the blank to 180 ° C, keep warm for 3 h, then blow by the blower Cold to normal temperature.
一、化学成分：First, the chemical composition:
本发明实施例1至7以及对比例1至3的渗碳合金钢的化学成分如表1所示。The chemical compositions of the carburized alloy steels of Examples 1 to 7 and Comparative Examples 1 to 3 of the present invention are shown in Table 1.
表1化学成分表Table 1 chemical composition table
Figure PCTCN2015082298-appb-000001
Figure PCTCN2015082298-appb-000001
Figure PCTCN2015082298-appb-000002
Figure PCTCN2015082298-appb-000002
二、力学性能：Second, the mechanical properties:
按照GB/T228-2010《金属材料室温拉伸试验方法》对本发明实施例1至7以及对比例1至3的渗碳合金钢进行力学性能测试，结果如表2所示。其中，Rm：抗拉强度；Rp0.2：规定非比例延伸率为0.2％的拉伸强度，即反映本发明的屈服强度；A：断后伸长率；Z：断面收缩率；KV2：冲击吸收能量，V型缺口，缺口深度2mm。The mechanical properties of the carburized alloy steels of Examples 1 to 7 and Comparative Examples 1 to 3 of the present invention were tested in accordance with GB/T 228-2010 "Metal Material Tensile Test Method", and the results are shown in Table 2. Wherein R m : tensile strength; R p0.2 : tensile strength of 0.2% of non-proportional elongation, ie, yield strength of the present invention; A: elongation after fracture; Z: reduction of area; KV 2 : Shock absorption energy, V-shaped notch, notch depth 2mm.
由表2可知，本发明的渗碳合金钢由于成分配比更为合理，实施例1-7的Rp0.2(MPa)相对对比例1-3具有明显提升，具有较高的屈服强度的同时冲击吸收能量KV2(J)并不下降甚至有所提高，因此，反映本发明实施例的合金钢屈强比高；并且，在其他力学性能方面不存在下降，例如对于抗拉强度Rm，实施例1、实施例2-7均相对对比例1-3基本相同或达到提升，仅实施例2的合金钢的碳含量较高而略低，因此，保持较好的韧性。It can be seen from Table 2 that the carburized alloy steel of the present invention is more reasonable in the distribution ratio, and R p0.2 (MPa) of Examples 1-7 has a significant improvement relative to Comparative Examples 1-3, and has a high yield strength. At the same time, the impact absorption energy KV 2 (J) does not decrease or even increases, and therefore, the alloy steel reflecting the embodiment of the present invention has a high yield ratio; and, there is no decrease in other mechanical properties, for example, tensile strength R m All of Example 1 and Examples 2-7 were substantially the same or improved relative to Comparative Examples 1-3, and only the alloy steel of Example 2 had a relatively high carbon content and was slightly lower, and therefore, maintained good toughness.
表2力学性能表Table 2 mechanical properties table
Figure PCTCN2015082298-appb-000003
Figure PCTCN2015082298-appb-000003
Figure PCTCN2015082298-appb-000004
Figure PCTCN2015082298-appb-000004
三、淬透性：Third, hardenability:
按照GB/T225-2006《钢的淬透性末端淬火试验方法》对本发明实施例1至实施例7以及对比例1至3的渗碳合金钢的淬透性进行测定。The hardenability of the carburized alloy steels of Examples 1 to 7 and Comparative Examples 1 to 3 of the present invention was measured in accordance with GB/T 225-2006 "Testing Method for Hardenability End Quenching of Steel".
如图1所示，本发明的渗碳合金钢与对比例1至3的渗碳合金钢相比淬透性更加优越，且ΔHRC(J1.5-J50)≤3。As shown in Fig. 1, the carburized alloy steel of the present invention is superior in hardenability to the carburized alloy steels of Comparative Examples 1 to 3, and ΔHRC (J1.5-J50) ≤ 3.
结合图1和图2所示，所有实施例1-7的渗碳合金钢在距端淬距离为0-50mm的范围内，其硬度均大于41，随着距端淬距离增大，硬度下降较慢。因此，反映本发明实施例的渗碳合金钢具有良好的淬透性。1 and 2, all of the carburized alloy steels of Examples 1-7 have a hardness of more than 41 in the range of 0-50 mm from the end, and the hardness decreases as the quenching distance increases. Slower. Therefore, the carburized alloy steel reflecting the embodiment of the present invention has good hardenability.
四、内氧化性：Fourth, internal oxidation:
按照GB/T25744-2010《钢件渗碳淬火回火金相检验》对本发明的实施例1至实施例7和对比例1的渗碳合金钢的内部氧化深度与渗碳层深度进行测定。实施例1和对比例1在每个相同的渗碳条件下，取了三个试样测量内氧化深度。The internal oxidation depth and the depth of the carburized layer of the carburized alloy steels of Examples 1 to 7 and Comparative Example 1 of the present invention were measured in accordance with GB/T 25744-2010 "Carbon carburizing quenching and tempering metallographic test". Example 1 and Comparative Example 1 Three samples were taken to measure the internal oxidation depth under each of the same carburizing conditions.
如图3和图4所示，在相同的渗碳层深度下，本发明实施例1中 的内氧化深度都远小于17Cr2Ni2Mo的内氧化层深度，且其内氧化层深度的波动也较小。As shown in FIG. 3 and FIG. 4, in the same carburized layer depth, in the first embodiment of the present invention The internal oxidation depth is much smaller than the internal oxide layer depth of 17Cr2Ni2Mo, and the fluctuation of the inner oxide layer depth is also small.
如图5所示，其中给出了实施例1至实施例7的渗碳合金钢在0.5mm、1.2mm、1.8mm、2.5mm、3.2mm的渗碳深度下的相应氧深度。所有实施例1至实施例7均具有较小的内氧化层深度。As shown in Fig. 5, the respective oxygen depths of the carburized alloy steels of Examples 1 to 7 at carburized depths of 0.5 mm, 1.2 mm, 1.8 mm, 2.5 mm, and 3.2 mm are shown. All of Examples 1 through 7 have a small inner oxide depth.
由此可见，本发明的渗碳合金钢与对比例1的渗碳合金钢相比在内氧化方面取得了很大的进步。From this, it can be seen that the carburized alloy steel of the present invention has made great progress in internal oxidation as compared with the carburized alloy steel of Comparative Example 1.
五、晶粒度：5. Grain size:
按照GB/T6394-2002《金属平均晶粒度测定法》对本发明实施例1至实施例7的晶粒度级别和晶粒平均直径进行测定。The grain size grade and the average grain diameter of Examples 1 to 7 of the present invention were measured in accordance with GB/T6394-2002 "Metal Average Grain Size Measurement Method".
如图6所示，本发明的实施例1的渗碳合金钢在930℃保温8h后晶粒度为9级(大于5级)，说明其是本质细晶钢，且其在1020℃～1050℃的温度区间内晶粒度都在6级以上，这说明本发明的渗碳合金钢可进行高温渗碳且不恶化材料的性能，例如在本实施例1的860℃的淬火条件(奥氏体化温度)下，其晶粒平均直径小于14微米。因此，具有良好的抗高温晶粒长大特性。As shown in FIG. 6, the carburized alloy steel of Example 1 of the present invention has a grain size of 9 grades (greater than 5 grades) after being kept at 930 ° C for 8 hours, indicating that it is an intrinsic fine grain steel, and it is at 1020 ° C to 1050. The grain size in the temperature range of °C is above 6 grades, which indicates that the carburized alloy steel of the present invention can perform high temperature carburization without deteriorating the properties of the material, for example, the quenching condition of 860 ° C in the first embodiment (Austen At body temperature, the average grain diameter is less than 14 microns. Therefore, it has good resistance to high temperature grain growth.
以下表三进一步给出了实施例1至实施例7的渗碳合金钢的晶粒尺寸。The grain sizes of the carburized alloy steels of Examples 1 to 7 are further given in Table 3 below.
表三晶粒尺寸Table 3 grain size
Figure PCTCN2015082298-appb-000005
Figure PCTCN2015082298-appb-000005
可以发现，实施例1至实施例7的渗碳合金钢都具有优异的抗晶粒长大性能。It was found that the carburized alloy steels of Examples 1 to 7 all have excellent resistance to grain growth.
本发明的渗碳合金钢及其制备方法不局限于上述各实施例。显然，上述实施例仅仅是为清楚地说明本发明所作的举例，而并非是对本发明的实施方式的限定。对于所属领域的普通技术人员来说，在上述说明的基础上还可以做出其它不同形式的变化或变动，如本发明的渗碳 合金钢的冶炼精炼工艺也可以采用中国专利文献CN102080188A(申请号：201010603965.1)所公开的方法。这里无需也无法对所有的实施方式予以穷举。而这些属于本发明的精神所引伸出的显而易见的变化或变动仍处于本发明的保护范围之中。 The carburized alloy steel of the present invention and a method for producing the same are not limited to the above embodiments. It is apparent that the above-described embodiments are merely illustrative of the invention and are not intended to limit the embodiments of the invention. Other variations or variations of the various forms, such as carburizing of the present invention, may also be made by those skilled in the art based on the above description. The smelting and refining process of the alloy steel can also be carried out by the method disclosed in Chinese Patent Publication No. CN102080188A (Application No.: 201010603965.1). There is no need and no way to exhaust all of the implementations. Obvious changes or variations that come within the spirit of the invention are still within the scope of the invention.

Claims (14)

  1. 一种渗碳合金钢，其特征在于，该合金钢的组分及其质量百分比为C：0.15％～0.25％，Si：≤0.30％，Mn：0.30％～1.20％，Cr：0.30％～1.50％，Ni：2.80％～3.80％，Mo：0.30％～1.00％，Al：0.01％～0.08％，以及V和Nb中的至少一种，余量为铁和不可避免的杂质；且当所述合金钢包含V时，V的质量百分比为0.05％～0.15％，当上述合金钢包含Nb时，Nb的质量百分比为0.025％～0.10％，并且所述V、Nb和Al的质量百分比含量符合V+Nb+Al≤0.30％。A carburized alloy steel, characterized in that the composition of the alloy steel and its mass percentage are C: 0.15% to 0.25%, Si: ≤ 0.30%, Mn: 0.30% to 1.20%, Cr: 0.30% to 1.50 %, Ni: 2.80% to 3.80%, Mo: 0.30% to 1.00%, Al: 0.01% to 0.08%, and at least one of V and Nb, the balance being iron and unavoidable impurities; When the alloy steel contains V, the mass percentage of V is 0.05% to 0.15%, and when the above alloy steel contains Nb, the mass percentage of Nb is 0.025% to 0.10%, and the mass percentage of the V, Nb and Al is in accordance with V. +Nb+Al≤0.30%.
  2. 根据权利要求1所述的渗碳合金钢，其特征在于，所述合金钢中的Al的质量百分比含量为0.02％～0.05％；所述V、Nb和Al的质量百分比含量符合V+Nb+Al≤0.20％。The carburized alloy steel according to claim 1, wherein a mass percentage of Al in the alloy steel is 0.02% to 0.05%; and a mass percentage of the V, Nb, and Al is in accordance with V+Nb+ Al ≤ 0.20%.
  3. 根据权利要求1所述的渗碳合金钢，其特征在于，所述合金钢中的C的质量百分比含量为0.15％～0.23％，Si的质量百分比含量为≤0.25％。The carburized alloy steel according to claim 1, wherein a content percentage of C in the alloy steel is 0.15% to 0.23%, and a mass percentage of Si is ≤0.25%.
  4. 根据权利要求1所述的渗碳合金钢，其特征在于，所述合金钢中的Mn的质量百分比含量为0.40％～1.00％，Cr的质量百分比含量为0.40％～1.20％。The carburized alloy steel according to claim 1, wherein the alloy steel has a mass percentage of Mn of 0.40% to 1.00% and a mass percentage of Cr of 0.40% to 1.20%.
  5. 根据权利要求1所述的渗碳合金钢，其特征在于，所述合金钢中的Ni的质量百分比含量为3.00％～3.80％，Mo的质量百分比含量为0.40％～0.80％。The carburized alloy steel according to claim 1, wherein a mass percentage of Ni in the alloy steel is 3.00% to 3.80%, and a mass percentage of Mo is 0.40% to 0.80%.
  6. 根据权利要求1所述的渗碳合金钢，其特征在于，所述合金钢中的杂质包括P和S元素，其中P的质量百分比含量为≤0.015％，S的质量百分比含量为≤0.010％。The carburized alloy steel according to claim 1, wherein the impurities in the alloy steel include P and S elements, wherein a mass percentage of P is ≤0.015%, and a mass percentage of S is ≤0.010%.
  7. 根据权利要求6所述的渗碳合金钢，其特征在于，所述合金钢中的杂质还包括N、O和H元素，其中N的质量百分比含量为≤0.02％，O的质量百分比含量为≤0.002％，H的质量百分比含量为≤0.0002％。The carburized alloy steel according to claim 6, wherein the impurities in the alloy steel further comprise N, O and H elements, wherein the mass percentage of N is ≤ 0.02%, and the mass percentage of O is ≤ 0.002%, the mass percentage content of H is ≤0.0002%.
  8. 根据权利要求7所述的渗碳合金钢，其特征在于，所述N的质量百分比含量为≤0.01％。The carburized alloy steel according to claim 7, wherein the mass percentage of N is ≤0.01%.
  9. 一种上述权利要求1到8中任一项所述的渗碳合金钢的制备方法，包括以下步骤： A method of preparing a carburized alloy steel according to any one of claims 1 to 8, comprising the steps of:
    A.根据合金钢的组分和含量进行配料，采用冶炼和精炼工艺进行合金熔炼；A. According to the composition and content of the alloy steel, the alloy is smelted by the smelting and refining process;
    B.浇注钢锭，将钢锭轧制成毛坯；B. pouring a steel ingot to roll the steel ingot into a blank;
    C.正火回火处理；和C. normalizing tempering; and
    D.淬火回火处理，其中，所述淬火回火处理是先将毛坯升温至800℃～860℃，保温0.8h～1.5h后，放入快速淬火油中冷却至快速淬火油的使用温度，然后取出毛坯再进行回火处理。D. quenching and tempering treatment, wherein the quenching and tempering treatment is to first raise the billet to 800 ° C ~ 860 ° C, after the temperature of 0.8 h ~ 1.5 h, put into the rapid quenching oil to cool to the use temperature of the rapid quenching oil, The blank is then removed and tempered.
  10. 根据权利要求9所述的渗碳合金钢的制备方法，其特征在于，所述正火回火处理是将毛坯升温至900℃～960℃，保温0.8h～1.5h后，风冷至室温，再将所述毛坯升温至630℃～750℃，保温0.8h～1.5h后，风冷至室温。The method for preparing a carburized alloy steel according to claim 9, wherein the normalizing and tempering treatment is to raise the temperature of the blank to 900 ° C to 960 ° C, heat the temperature for 0.8 h to 1.5 h, and then air-cool to room temperature. The billet is further heated to 630 ° C to 750 ° C, held for 0.8 h to 1.5 h, and then air cooled to room temperature.
  11. 根据权利要求10所述的渗碳合金钢的制备方法，其特征在于，所述淬火回火处理中，在回火时将毛坯升温至160℃～220℃，保温2.5h～3.5h后，风冷至室温。The method for preparing a carburized alloy steel according to claim 10, wherein in the quenching and tempering treatment, the billet is heated to 160 ° C to 220 ° C during tempering, and the wind is kept for 2.5 h to 3.5 h. Cool to room temperature.
  12. 根据权利要求9所述的渗碳合金钢的制备方法，其特征在于，所述快速淬火油的使用温度为40℃～100℃。The method for producing a carburized alloy steel according to claim 9, wherein the rapid quenching oil is used at a temperature of from 40 ° C to 100 ° C.
  13. 根据权利要求9所述的渗碳合金钢的制备方法，其特征在于，所述步骤A中，所述冶炼和精炼工艺采用电炉进行冶炼和采用钢包精炼炉+真空脱气炉进行精炼的工艺。The method for preparing a carburized alloy steel according to claim 9, wherein in the step A, the smelting and refining process is performed by an electric furnace for smelting and a refining process using a ladle refining furnace + a vacuum degassing furnace.
  14. 一种上述权利要求1到8中任一项所述的渗碳合金钢的应用，其特征在于，用于制造重载齿轮。 Use of the carburized alloy steel according to any one of claims 1 to 8, characterized in that it is used for the manufacture of heavy duty gears.
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Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107225148A (en) * 2017-06-01 2017-10-03 马鞍山钢铁股份有限公司 A kind of milling method of 22CrMoH pinion steels
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CN114196889A (en) * 2021-11-29 2022-03-18 湖南华菱涟源钢铁有限公司 Hot-rolled steel sheet material, method for producing same and product
CN114411046A (en) * 2022-01-19 2022-04-29 丹阳市曙光新材料科技有限公司 Process for smelting high-speed steel by using intermediate frequency furnace-LF furnace-VD furnace

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Publication number Priority date Publication date Assignee Title
CN104109816B (en) * 2014-06-26 2017-05-17 南车戚墅堰机车车辆工艺研究所有限公司 Carburizing alloy steel, and preparation method and application thereof
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CN105420633A (en) * 2015-11-18 2016-03-23 宁波瑞尔汽车零部件有限公司 Screw
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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0328347A (en) * 1989-06-23 1991-02-06 Sumitomo Metal Ind Ltd Carburized case hardening steel excellent in delayed fracture resistance
JPH1150191A (en) * 1997-08-05 1999-02-23 Nippon Steel Corp Carburized axial parts and production thereof
JP2001200348A (en) * 2000-01-17 2001-07-24 Daido Steel Co Ltd Gear couple excellent in surface fatigue strength
CN1441077A (en) * 2002-02-28 2003-09-10 尾上广司 High strength therad steel and high strength screw
CN1861830A (en) * 2006-06-22 2006-11-15 钢铁研究总院 Steel for heavy loading gear
CN102162069A (en) * 2010-02-23 2011-08-24 宝山钢铁股份有限公司 Flying-shear main-transmission gearwheel steel and preparation method thereof
CN104109816A (en) * 2014-06-26 2014-10-22 南车戚墅堰机车车辆工艺研究所有限公司 Carburizing alloy steel, and preparation method and application thereof

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2630670B2 (en) * 1990-07-27 1997-07-16 三菱製鋼 株式会社 Steel with high fatigue strength for carburized gears
JP3521190B2 (en) * 1999-09-16 2004-04-19 三菱製鋼室蘭特殊鋼株式会社 High-strength chromium steel for carburizing and carbonitriding
CN100365150C (en) * 2005-04-22 2008-01-30 常曙光 Heavy-load gear steel
JP4728883B2 (en) * 2006-06-16 2011-07-20 新日本製鐵株式会社 Carburized and hardened steel and carburized parts with excellent low cycle fatigue properties
CN102168069B (en) * 2010-12-09 2012-07-04 浙江大学医学院附属第二医院 Cell strain capable of inducing and realizing dual-stabilization of P53 expression and construction method and application thereof
CN102226252B (en) * 2011-06-10 2013-03-20 钢铁研究总院 High-toughness carburized bearing steel with ultra-long contact fatigue life and preparation method thereof
CN102560282A (en) * 2012-01-30 2012-07-11 杜树芳 Nitrided gear steel and heat treatment method thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0328347A (en) * 1989-06-23 1991-02-06 Sumitomo Metal Ind Ltd Carburized case hardening steel excellent in delayed fracture resistance
JPH1150191A (en) * 1997-08-05 1999-02-23 Nippon Steel Corp Carburized axial parts and production thereof
JP2001200348A (en) * 2000-01-17 2001-07-24 Daido Steel Co Ltd Gear couple excellent in surface fatigue strength
CN1441077A (en) * 2002-02-28 2003-09-10 尾上广司 High strength therad steel and high strength screw
CN1861830A (en) * 2006-06-22 2006-11-15 钢铁研究总院 Steel for heavy loading gear
CN102162069A (en) * 2010-02-23 2011-08-24 宝山钢铁股份有限公司 Flying-shear main-transmission gearwheel steel and preparation method thereof
CN104109816A (en) * 2014-06-26 2014-10-22 南车戚墅堰机车车辆工艺研究所有限公司 Carburizing alloy steel, and preparation method and application thereof

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107225148A (en) * 2017-06-01 2017-10-03 马鞍山钢铁股份有限公司 A kind of milling method of 22CrMoH pinion steels
CN107225148B (en) * 2017-06-01 2019-02-19 马鞍山钢铁股份有限公司 A kind of milling method of 22CrMoH pinion steel
CN112359178A (en) * 2020-10-23 2021-02-12 长沙万钛工程机械有限公司 Heat treatment process for steel workpiece
CN112322867A (en) * 2020-10-26 2021-02-05 武汉重工铸锻有限责任公司 Heat treatment process for improving comprehensive mechanical properties of Cr-Ni-Mo large-scale forging for nuclear power
CN114196889A (en) * 2021-11-29 2022-03-18 湖南华菱涟源钢铁有限公司 Hot-rolled steel sheet material, method for producing same and product
CN114411046A (en) * 2022-01-19 2022-04-29 丹阳市曙光新材料科技有限公司 Process for smelting high-speed steel by using intermediate frequency furnace-LF furnace-VD furnace

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