WO2019153764A1 - Hot-rolled, abrasion-resistant steel plate and manufacturing method thereof - Google Patents

Hot-rolled, abrasion-resistant steel plate and manufacturing method thereof Download PDF

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WO2019153764A1
WO2019153764A1 PCT/CN2018/108991 CN2018108991W WO2019153764A1 WO 2019153764 A1 WO2019153764 A1 WO 2019153764A1 CN 2018108991 W CN2018108991 W CN 2018108991W WO 2019153764 A1 WO2019153764 A1 WO 2019153764A1
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resistant steel
hot
rolled
steel sheet
wear
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PCT/CN2018/108991
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French (fr)
Chinese (zh)
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孙超
王从道
段东明
江姗
党军
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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a wear-resistant steel technology, in particular to a hot-rolled wear-resistant steel plate and a manufacturing method thereof.
  • Wear-resistant steel is widely used in industries with metallurgical, mining, electric power, agriculture and other wear conditions, such as manufacturing dump trucks, scraper conveyors, bulldozers, loaders, excavators, shield machines, roadheaders, harvesters and cement. Ball mill and other devices.
  • the most important mechanical property index of wear-resistant steel is hardness.
  • the wear-resistant steel of the standard GB/T24186 grade NM400 has a surface Brinell hardness HBW of 370-430. The high hardness ensures that the wear-resistant steel has a longer service life under service conditions.
  • wear-resistant steel One of the more materials used in wear-resistant steel is high-manganese wear-resistant steel, invented by the British Hadfield in 1883.
  • the wear-resistant steel generally has a Mn content of more than 10%, has an austenite structure, and obtains a high hardness by a mechanism of deformation-induced phase transformation or twinning under high impact load, but has insufficient work hardening effect under a low impact load.
  • too high Mn content and C content make high manganese wear-resistant steel high in preparation cost.
  • Medium and low alloy wear-resistant steel is also a commonly used type of wear-resistant steel.
  • the wear-resistant steel generally has a Mn content of less than 2%, and in order to obtain high hardenability, a large amount of expensive alloying elements such as Cr, Ni, and Mo are added, so that the alloy cost is high.
  • high-manganese wear-resistant steel and medium-low alloy wear-resistant steel usually require heat treatment processes such as water toughness treatment and tempering treatment, and thus the process cost is high.
  • Patent No. CN 104884655 A entitled “High Manganese Wear-Resistant Steel with Excellent Weldability" discloses a high-manganese wear-resistant steel excellent in weldability, comprising 5-15% Mn, 16 ⁇ 33.5C The C, Mn content and C content of +Mn ⁇ 30 are both high, which obviously also makes the preparation cost of the high manganese wear-resistant steel too high.
  • Patent No. CN 105239014 A entitled “A Low Cost High Carbon Medium Manganese Wear-Resistant Steel and Its Hot-Rolled Sheet Manufacturing Method" discloses a high-carbon medium manganese wear-resistant steel and its hot-rolled sheet manufacturing method.
  • the C content is 0.7 to 0.9%
  • the Mn content is 7.0 to 9.0%.
  • the Mn content and the C content are also high
  • the steel plate is also added with 2.0 to 3.0% of Cr, which increases the alloy cost.
  • the solution treatment is required in the preparation method, and the process flow is complicated.
  • the authorization announcement number is CN 105039861 B, a patent entitled “A medium-manganese boron-containing low-alloy wear-resistant steel plate and a preparation method thereof", and the disclosed manganese-containing boron-containing low-alloy wear-resistant steel plate has a Mn content of 3.0 to 3.9%. It increases the hardenability by adding B element, increases the cost of the alloy, and also requires heat treatment in the preparation method, and the process flow is long.
  • the present invention provides a low-cost hot-rolled wear-resistant steel plate that ensures high hardness of the steel sheet while reducing alloy cost and process cost.
  • Another object of the present invention is to provide a method of manufacturing a hot rolled wear resistant steel sheet which shortens the process flow and reduces the manufacturing cost.
  • a hot-rolled wear-resistant steel plate according to the present invention comprises a chemical composition of 0.14 to 0.22% of C, 5.3 to 6.5% of Mn, 0.1 to 0.5% of Si, and 0.01 to 0.04. % Ti, as well as the balance of Fe and inevitable impurity elements.
  • the microstructure of the hot-rolled wear-resistant steel plate is martensite.
  • C and Mn are the most important alloying elements of the present invention.
  • the C element as an austenite stabilizing element can significantly improve the hardenability of steel, and the C atom also has a significant solid solution strengthening effect as a gap atom.
  • the Mn element, as an austenite stabilizing element can also significantly improve the hardenability of steel, and the Mn atom acts as a substitution atom for solid solution strengthening.
  • C and Mn are capable of forming carbides, thereby further increasing the hardness of the tissue.
  • the present invention controls the C content to be 0.14 to 0.22% and the Mn content to be 5.3 to 6.5%, so that the steel sheet can obtain the optimum hardenability and obtain a high hardness martensite structure.
  • Si is a deoxidizing element in the steel making process, and can also produce solid solution strengthening, but when the content is too high, the properties such as toughness are lowered. Therefore, the present invention controls the Si content to be 0.1 to 0.5%.
  • Ti forms TiN precipitates in steel, which can suppress austenite grain coarsening at high temperatures, which is advantageous for refining the martensite structure and improving the strength and hardness of martensite. A slight addition can work, and excessive addition will result in coarse inclusions. Therefore, the present invention controls the Ti content to be 0.01 to 0.04%.
  • the method for manufacturing the hot-rolled wear-resistant steel sheet of the present invention comprises the following steps:
  • the final rolling temperature is 820 ⁇ 870 ° C, the thickness of the steel plate after rolling is ⁇ 16mm;
  • the total deformation of the rolling is ⁇ 80%, so as to ensure sufficient recrystallization refining effect of the austenite grains during the rolling process.
  • the total deformation amount (thickness of slab - thickness of steel plate) ⁇ 100% / thickness of slab.
  • the cooling rate of the steel plate air cooling is not excessively large, in order to facilitate the precipitation of carbides in the martensite structure, further increase the hardness of the structure, and the thickness of the steel plate obtained after the juice extraction in the step (2) is further limited. It is 4 to 16 mm.
  • the alloy composition is simple, the alloy cost is greatly reduced, and the content of manganese and carbon as the main alloying elements is precision. Control, can obtain the best hardenability, and obtain a high-hardness martensite structure, so that the hot-rolled wear-resistant steel sheet of the present invention has high-hardness and has a remarkable feature of low cost, which is resistant to hot rolling.
  • the surface hardness of the milled steel plate can reach 370-430 HBW.
  • Example 1 is a photograph of an optical metallographic structure of a hot-rolled wear-resistant steel sheet of Example 1;
  • Example 2 is a photograph of an optical metallographic structure of a hot-rolled wear-resistant steel sheet of Example 2;
  • Example 3 is a photograph of an optical metallographic structure of a hot-rolled wear-resistant steel sheet of Example 3.
  • the inventors conducted intensive studies to solve the problems existing in the existing wear-resistant steel, and found that by precisely controlling the contents of manganese and carbon as main alloying elements, the best hardenability can be obtained, and a horse with high hardness can be obtained. Sterile tissue. By precisely controlling the alloying elements silicon and titanium, it is possible to refine and strengthen martensite and further increase the hardness of martensite. The present invention has been further proposed.
  • the hot-rolled wear-resistant steel sheet of the present invention contains, in weight percent, 0.14 to 0.22% of C, 5.3 to 6.5% of Mn, 0.1 to 0.5% of Si, 0.01 to 0.04% of Ti, and the balance. Fe and inevitable impurity elements.
  • the chemical composition is limited by the reason that C and Mn are the most important alloying elements of the present invention.
  • the C element as an austenite stabilizing element can significantly improve the hardenability of steel, and the C atom also has a significant solid solution strengthening effect as a gap atom.
  • the Mn element, as an austenite stabilizing element can also significantly improve the hardenability of steel, and the Mn atom acts as a substitution atom for solid solution strengthening.
  • C and Mn are capable of forming carbides, thereby further increasing the hardness of the tissue.
  • the present invention controls the C content to be 0.14 to 0.22% and the Mn content to be 5.3 to 6.5%, so that the steel sheet can obtain the optimum hardenability and obtain a high hardness martensite structure.
  • Si is a deoxidizing element in the steel making process, and can also produce solid solution strengthening, but when the content is too high, the properties such as toughness are lowered. Therefore, the present invention controls the Si content to be 0.1 to 0.5%.
  • Ti forms TiN precipitates in steel, which can suppress austenite grain coarsening at high temperatures, which is advantageous for refining the martensite structure and improving the strength and hardness of martensite. A slight addition can work, and excessive addition will result in coarse inclusions. Therefore, the present invention controls the Ti content to be 0.01 to 0.04%.
  • the method adopted includes the following steps:
  • the slab is heated at a temperature of 1030 to 1120 ° C, and the ratio of the heating time to the thickness of the slab is 0.9 to 1.3 min/mm; then the heated slab is rolled, and the finishing temperature is 820 to 870 ° C.
  • the total deformation of the rolling is ⁇ 80%, and the thickness of the steel sheet after rolling is 4 to 16 mm; and the steel sheet after rolling is air-cooled to room temperature.
  • the total deformation amount (thickness of slab - thickness of steel plate) ⁇ 100% / thickness of slab.
  • the mechanism of the manufacturing method is that a high temperature austenite structure is obtained when the billet is heated, and the alloy elements are homogenized by diffusion. If the heating temperature is too high or the holding time is too long, the high-temperature austenite grains will be too coarse, and the heating temperature is too low or the holding time is too short, which is not conducive to the homogenization of the alloying elements. Therefore, the heating temperature of the present invention is controlled at 1030 to 1120 ° C. The ratio of the heating time to the thickness of the slab is controlled to be 0.9 to 1.3 min/mm.
  • the billet After heating, the billet is rolled, and the finishing temperature is not lower than 830 ° C, so that the deformation temperature is in the austenite phase region, and the finish rolling temperature is not higher than 870 ° C, which can avoid excessive coarsening of recrystallized austenite.
  • Austenite grains are refined by recrystallization during rolling, and a total deformation amount of ⁇ 80% can ensure sufficient recrystallization refining effect. Due to the high hardenability of steel grades, the air cooling rate of steel plates of 16 mm and below reaches the cooling rate ( ⁇ 0.1 °C/s) required for martensitic transformation under the alloy composition. Therefore, austenite can be transformed into martensite during air cooling after rolling.
  • the cooling rate is not too large, which is favorable for the precipitation of carbides in the martensite structure and further increases the hardness of the structure.
  • the steel sheet After cooling to room temperature, the steel sheet obtained a martensitic structure having sufficient hardness, and the surface hardness of the steel sheet was HB-WH of 370-430.
  • Example 1 A slab having a thickness of 100 mm and a chemical composition of 0.17% C, 5.7% Mn, 0.22% Si, 0.019% Ti, and the balance Fe and impurity elements, at a temperature of 1080 ° C Heat down for 110 min.
  • the heated billet is rolled, and the rolling schedule is as shown in Table 1:
  • the total deformation was 89.3% and the finishing temperature was 846 °C. After rolling, it was air cooled to room temperature.
  • a hot-rolled wear-resistant steel sheet having a thickness of 10.7 mm was obtained, and the chemical composition contained 0.17% C, 5.9% Mn, 0.22% Si, 0.019% Ti, and the balance of Fe and impurity elements in terms of mass percentage.
  • the microstructure is all martensite as shown in Fig. 1.
  • the surface hardness of the steel plate is 409HBW.
  • Example 2 A slab having a thickness of 80 mm and a chemical composition of 0.14% C, 6.5% Mn, 0.1% Si, 0.04% Ti, and the balance Fe and impurity elements, at a temperature of 1120 ° C Heat down for 72 min.
  • the heated billet is rolled, and the rolling schedule is as shown in Table 2:
  • the total deformation amount is 80%, and the finishing temperature is 870 °C. After rolling, it was air cooled to room temperature.
  • a hot-rolled wear-resistant steel sheet having a thickness of 16 mm was obtained, and the chemical composition contained, by mass percentage, 0.14% C, 6.5% Mn, 0.1% Si, 0.04% Ti, and the balance Fe and impurity elements.
  • the microstructure is shown in Figure 2 as a martensite structure, and the surface hardness of the steel plate is 370 HBW.
  • Example 3 a slab having a thickness of 60 mm and a chemical composition of 0.22% C, 5.3% Mn, 0.5% Si, 0.01% Ti, and the balance Fe and impurity elements, at a temperature of 1030 ° C Heat down for 78 min.
  • the heated billet is rolled, and the rolling schedule is as shown in Table 3:
  • the total deformation was 93.3%, and the finishing temperature was 820 °C. After rolling, it was air cooled to room temperature.
  • a low-cost hot-rolled wear-resistant steel plate having a thickness of 4 mm is obtained, and the chemical composition contains 0.22% C, 5.3% Mn, 0.5% Si, 0.01% Ti, and the balance Fe and impurity elements in terms of mass percentage, and the microstructure is as shown in the figure. 3 shows a martensite structure, and the surface hardness of the steel plate is 430 HBW.

Abstract

Disclosed is a hot-rolled, abrasion-resistant steel plate and a manufacturing method thereof. The chemical composition of the steel sheet comprises, by weight percent: 0.14% to 0.22% of C, 5.3% to 6.5% of Mn, 0.1% to 0.5% of Si, and 0.01% to 0.04% of Ti, with the balance being Fe and unavoidable impurities. The method of manufacturing the steel plate uses air cooling instead of on-line quenching, and heat treatment is not required in the production.

Description

一种热轧耐磨钢板及其制造方法Hot rolled wear resistant steel plate and manufacturing method thereof 技术领域Technical field
本发明涉及一种耐磨钢技术，具体涉及一种热轧耐磨钢板及其制造方法。The invention relates to a wear-resistant steel technology, in particular to a hot-rolled wear-resistant steel plate and a manufacturing method thereof.
背景技术Background technique
耐磨钢广泛应用于冶金、矿山、电力、农业等存在磨损工况的行业中，如制造自卸车、刮板运输机、推土机，装载机，挖掘机、盾构机、掘进机、收割机及水泥球磨机等装置。耐磨钢最主要的力学性能指标为硬度，例如，标准GB/T24186中牌号为NM400的耐磨钢的表面布氏硬度HBW为370～430。高硬度保证了耐磨钢在服役条件下有更长的使用寿命。Wear-resistant steel is widely used in industries with metallurgical, mining, electric power, agriculture and other wear conditions, such as manufacturing dump trucks, scraper conveyors, bulldozers, loaders, excavators, shield machines, roadheaders, harvesters and cement. Ball mill and other devices. The most important mechanical property index of wear-resistant steel is hardness. For example, the wear-resistant steel of the standard GB/T24186 grade NM400 has a surface Brinell hardness HBW of 370-430. The high hardness ensures that the wear-resistant steel has a longer service life under service conditions.
耐磨钢中应用较多材料之一是高锰耐磨钢，由英国人哈德菲尔德在1883年发明。这种耐磨钢的Mn含量通常高于10％，具有奥氏体组织，在高冲击载荷下通过形变诱发相变或孪晶的机制获得高硬度，但在低冲击载荷下加工硬化效果不足。同时，过高的Mn含量及C含量也使得高锰耐磨钢制备成本高。中低合金耐磨钢也是常用的一类耐磨钢。这类耐磨钢的Mn含量通常在2％以内，而为了得到高淬透性，添加了大量Cr、Ni、Mo等价格高昂的合金元素，因而合金成本较高。此外，在制备工艺方面，高锰耐磨钢和中低合金耐磨钢通常需要经过水韧处理、回火处理等热处理工序，因而工艺成本较高。One of the more materials used in wear-resistant steel is high-manganese wear-resistant steel, invented by the British Hadfield in 1883. The wear-resistant steel generally has a Mn content of more than 10%, has an austenite structure, and obtains a high hardness by a mechanism of deformation-induced phase transformation or twinning under high impact load, but has insufficient work hardening effect under a low impact load. At the same time, too high Mn content and C content make high manganese wear-resistant steel high in preparation cost. Medium and low alloy wear-resistant steel is also a commonly used type of wear-resistant steel. The wear-resistant steel generally has a Mn content of less than 2%, and in order to obtain high hardenability, a large amount of expensive alloying elements such as Cr, Ni, and Mo are added, so that the alloy cost is high. In addition, in the preparation process, high-manganese wear-resistant steel and medium-low alloy wear-resistant steel usually require heat treatment processes such as water toughness treatment and tempering treatment, and thus the process cost is high.
公开号为CN 104884655 A，名为《焊接性优异的高锰耐磨钢》的专利申请，公开了一种焊接性优异的高锰耐磨钢，包含5～15％的Mn、16≤33.5C+Mn≤30的C，Mn含量及C含量都偏高，显然也会使得其高锰耐磨钢的制备成本过高。Patent No. CN 104884655 A, entitled "High Manganese Wear-Resistant Steel with Excellent Weldability", discloses a high-manganese wear-resistant steel excellent in weldability, comprising 5-15% Mn, 16≤33.5C The C, Mn content and C content of +Mn ≤ 30 are both high, which obviously also makes the preparation cost of the high manganese wear-resistant steel too high.
公开号为CN 105239014 A，名为《一种低成本高碳中锰耐磨钢及其热轧板制造方法》的专利申请，公开了一种高碳中锰耐磨钢及其热轧板制造方法。其中C含量为0.7～0.9％，Mn含量为7.0～9.0％。同样其Mn含量及C含量也都偏高，此外该钢板还添加了2.0～3.0％的Cr，增加了合金成本。且其制备方法中需要固溶处理，工艺流程较为复杂。Patent No. CN 105239014 A, entitled "A Low Cost High Carbon Medium Manganese Wear-Resistant Steel and Its Hot-Rolled Sheet Manufacturing Method", discloses a high-carbon medium manganese wear-resistant steel and its hot-rolled sheet manufacturing method. The C content is 0.7 to 0.9%, and the Mn content is 7.0 to 9.0%. Similarly, the Mn content and the C content are also high, and the steel plate is also added with 2.0 to 3.0% of Cr, which increases the alloy cost. Moreover, the solution treatment is required in the preparation method, and the process flow is complicated.
授权公告号为CN 105039861 B，名为《一种中锰含硼低合金耐磨钢板及其制备方法》的专利，公开的中锰含硼低合金耐磨钢板的Mn含量为3.0～3.9％，其通过添加B元素提高淬透性，增加了合金成本，此外其制备方法中也需要经过 热处理，工艺流程较长。The authorization announcement number is CN 105039861 B, a patent entitled "A medium-manganese boron-containing low-alloy wear-resistant steel plate and a preparation method thereof", and the disclosed manganese-containing boron-containing low-alloy wear-resistant steel plate has a Mn content of 3.0 to 3.9%. It increases the hardenability by adding B element, increases the cost of the alloy, and also requires heat treatment in the preparation method, and the process flow is long.
发明内容Summary of the invention
发明目的：为了克服现有技术的缺陷，本发明提供一种低成本的热轧耐磨钢板，保证钢板具有高硬度的同时，降低了合金成本和工艺成本。OBJECT OF THE INVENTION: To overcome the deficiencies of the prior art, the present invention provides a low-cost hot-rolled wear-resistant steel plate that ensures high hardness of the steel sheet while reducing alloy cost and process cost.
本发明的另一目的是提供一种热轧耐磨钢板的制造方法，该方法缩短了工艺流程，降低了制造成本。Another object of the present invention is to provide a method of manufacturing a hot rolled wear resistant steel sheet which shortens the process flow and reduces the manufacturing cost.
技术方案：本发明所述的一种热轧耐磨钢板，其化学成分以重量百分比计包含有：0.14～0.22％的C、5.3～6.5％的Mn、0.1～0.5％的Si、0.01～0.04％的Ti，以及余量的Fe和不可避免的杂质元素。Technical Solution: A hot-rolled wear-resistant steel plate according to the present invention comprises a chemical composition of 0.14 to 0.22% of C, 5.3 to 6.5% of Mn, 0.1 to 0.5% of Si, and 0.01 to 0.04. % Ti, as well as the balance of Fe and inevitable impurity elements.
其中，所述热轧耐磨钢板的微观组织结构为马氏体。Wherein, the microstructure of the hot-rolled wear-resistant steel plate is martensite.
本发明中化学成分的限定理由如下：The reasons for limiting the chemical composition in the present invention are as follows:
C和Mn是本发明最重要的合金元素。C元素作为奥氏体稳定化元素能够显著提高钢的淬透性，C原子作为间隙原子还具有显著的固溶强化作用。Mn元素作为奥氏体稳定化元素同样能够显著提高钢的淬透性，同时Mn原子作为置换原子发挥固溶强化作用。此外，C和Mn能够形成碳化物，从而进一步提高组织硬度。而Mn、C含量过低时，钢的淬透性降低，不利于得到马氏体组织，且马氏体的硬度也偏低；Mn、C含量过高时，残余奥氏体增多，马氏体比例相应减少。所以本发明控制C含量为0.14～0.22％、Mn含量为5.3～6.5％，使钢板能够获得最佳的淬透性并获得高硬度的马氏体组织。C and Mn are the most important alloying elements of the present invention. The C element as an austenite stabilizing element can significantly improve the hardenability of steel, and the C atom also has a significant solid solution strengthening effect as a gap atom. The Mn element, as an austenite stabilizing element, can also significantly improve the hardenability of steel, and the Mn atom acts as a substitution atom for solid solution strengthening. In addition, C and Mn are capable of forming carbides, thereby further increasing the hardness of the tissue. When the content of Mn and C is too low, the hardenability of steel is lowered, which is not conducive to obtaining martensite structure, and the hardness of martensite is also low; when the content of Mn and C is too high, the retained austenite is increased, Markov The proportion of the body is correspondingly reduced. Therefore, the present invention controls the C content to be 0.14 to 0.22% and the Mn content to be 5.3 to 6.5%, so that the steel sheet can obtain the optimum hardenability and obtain a high hardness martensite structure.
Si在炼钢过程中为脱氧元素，还能够产生固溶强化作用，但含量过高时会降低韧性等性能。因此，本发明将Si含量控制为0.1～0.5％。Si is a deoxidizing element in the steel making process, and can also produce solid solution strengthening, but when the content is too high, the properties such as toughness are lowered. Therefore, the present invention controls the Si content to be 0.1 to 0.5%.
Ti在钢中形成TiN析出，能够抑制高温下奥氏体晶粒粗化，从而有利于细化马氏体组织，提高马氏体的强度及硬度。微量添加就能够发挥作用，过量添加将导致夹杂物粗大。所以，本发明将Ti含量控制为0.01～0.04％。Ti forms TiN precipitates in steel, which can suppress austenite grain coarsening at high temperatures, which is advantageous for refining the martensite structure and improving the strength and hardness of martensite. A slight addition can work, and excessive addition will result in coarse inclusions. Therefore, the present invention controls the Ti content to be 0.01 to 0.04%.
而本发明的热轧耐磨钢板的制造方法，包括下述步骤：The method for manufacturing the hot-rolled wear-resistant steel sheet of the present invention comprises the following steps:
(1)将板坯在1030～1120℃的温度条件下加热，加热时间与板坯厚度的比值为0.9～1.3min/mm；(1) heating the slab at a temperature of 1030 to 1120 ° C, the ratio of the heating time to the thickness of the slab is 0.9 to 1.3 min / mm;
(2)然后对加热后的板坯进行轧制，终轧温度为820～870℃，轧制后得到钢板的厚度≤16mm；(2) then rolling the heated slab, the final rolling temperature is 820 ~ 870 ° C, the thickness of the steel plate after rolling is ≤ 16mm;
(3)将轧制后的钢板空冷至室温。(3) The rolled steel sheet is air-cooled to room temperature.
进一步的，轧制的总变形量≥80％，以能够保证轧制过程中奥氏体晶粒具有足够的再结晶细化效果。Further, the total deformation of the rolling is ≥80%, so as to ensure sufficient recrystallization refining effect of the austenite grains during the rolling process.
其中，总变形量＝(板坯的厚度-钢板的厚度)×100％/板坯的厚度。Among them, the total deformation amount = (thickness of slab - thickness of steel plate) × 100% / thickness of slab.
为了控制步骤(3)中，钢板空冷的冷却速度不至于过大，以有利于马氏体组织中碳化物的析出，进一步提高组织硬度，步骤(2)中榨汁后得到的钢板厚度进一步限定为4～16mm。In order to control the step (3), the cooling rate of the steel plate air cooling is not excessively large, in order to facilitate the precipitation of carbides in the martensite structure, further increase the hardness of the structure, and the thickness of the steel plate obtained after the juice extraction in the step (2) is further limited. It is 4 to 16 mm.
有益效果：本发明在合金方面，通过采用Mn元素代替价格昂贵的Cr、Ni、Mo等元素，合金成分简单，大大降低了合金成本；且通过对作为主要合金元素的锰和碳的含量进行精密控制，能够获得最佳的淬透性，并且获得高硬度的马氏体组织，从而使得本发明的热轧耐磨钢板在具备高硬度的同时还具备低成本的显著特点，所述热轧耐磨钢板的表面布氏硬度可以达到370～430HBW。而在工艺方面，利用钢种淬透性高的特点，在一定厚度规格范围内采用空冷代替在线淬火，降低了能耗；在马氏体相变温度区间采取空冷方式也有利于钢板板形的控制，降低了对矫直工艺的要求，从而进一步降低了成本。此外，工艺方面不需要热处理，因而大大缩短了工艺流程并降低了成本。Advantageous Effects: In the aspect of the alloy, by using Mn element instead of expensive elements such as Cr, Ni, Mo, etc., the alloy composition is simple, the alloy cost is greatly reduced, and the content of manganese and carbon as the main alloying elements is precision. Control, can obtain the best hardenability, and obtain a high-hardness martensite structure, so that the hot-rolled wear-resistant steel sheet of the present invention has high-hardness and has a remarkable feature of low cost, which is resistant to hot rolling. The surface hardness of the milled steel plate can reach 370-430 HBW. In terms of technology, the use of high hardness of steel, the use of air cooling in a certain thickness range instead of on-line quenching, reducing energy consumption; air cooling in the martensitic transformation temperature range is also conducive to the shape of the steel plate Control reduces the need for straightening processes, further reducing costs. In addition, no heat treatment is required in the process, which greatly shortens the process and reduces costs.
附图说明DRAWINGS
图1是实施例1的热轧耐磨钢板的光学金相组织照片；1 is a photograph of an optical metallographic structure of a hot-rolled wear-resistant steel sheet of Example 1;
图2是实施例2的热轧耐磨钢板的光学金相组织照片；2 is a photograph of an optical metallographic structure of a hot-rolled wear-resistant steel sheet of Example 2;
图3是实施例3的热轧耐磨钢板的光学金相组织照片。3 is a photograph of an optical metallographic structure of a hot-rolled wear-resistant steel sheet of Example 3.
具体实施方式Detailed ways
发明人为了解决现有耐磨钢存在的问题而进行深入研究，发现了通过对作为主要合金元素的锰和碳的含量进行精密控制，能够获得最佳的淬透性，并且获得高硬度的马氏体组织。通过对合金元素硅和钛的精密控制，能够细化并强化马氏体，进一步提高马氏体的硬度。进而提出了本发明。The inventors conducted intensive studies to solve the problems existing in the existing wear-resistant steel, and found that by precisely controlling the contents of manganese and carbon as main alloying elements, the best hardenability can be obtained, and a horse with high hardness can be obtained. Sterile tissue. By precisely controlling the alloying elements silicon and titanium, it is possible to refine and strengthen martensite and further increase the hardness of martensite. The present invention has been further proposed.
本发明的热轧耐磨钢板，其化学成分以重量百分比计包含有：0.14～0.22％的C、5.3～6.5％的Mn、0.1～0.5％的Si、0.01～0.04％的Ti，以及余量的Fe和不可避免的杂质元素。The hot-rolled wear-resistant steel sheet of the present invention contains, in weight percent, 0.14 to 0.22% of C, 5.3 to 6.5% of Mn, 0.1 to 0.5% of Si, 0.01 to 0.04% of Ti, and the balance. Fe and inevitable impurity elements.
其化学成分的限定理由是：C和Mn是本发明最重要的合金元素。C元素作 为奥氏体稳定化元素能够显著提高钢的淬透性，C原子作为间隙原子还具有显著的固溶强化作用。Mn元素作为奥氏体稳定化元素同样能够显著提高钢的淬透性，同时Mn原子作为置换原子发挥固溶强化作用。此外，C和Mn能够形成碳化物，从而进一步提高组织硬度。而Mn、C含量过低时，钢的淬透性降低，不利于得到马氏体组织，且马氏体的硬度也偏低；Mn、C含量过高时，残余奥氏体增多，马氏体比例相应减少。所以本发明控制C含量为0.14～0.22％、Mn含量为5.3～6.5％，使钢板能够获得最佳的淬透性并获得高硬度的马氏体组织。The chemical composition is limited by the reason that C and Mn are the most important alloying elements of the present invention. The C element as an austenite stabilizing element can significantly improve the hardenability of steel, and the C atom also has a significant solid solution strengthening effect as a gap atom. The Mn element, as an austenite stabilizing element, can also significantly improve the hardenability of steel, and the Mn atom acts as a substitution atom for solid solution strengthening. In addition, C and Mn are capable of forming carbides, thereby further increasing the hardness of the tissue. When the content of Mn and C is too low, the hardenability of steel is lowered, which is not conducive to obtaining martensite structure, and the hardness of martensite is also low; when the content of Mn and C is too high, the retained austenite is increased, Markov The proportion of the body is correspondingly reduced. Therefore, the present invention controls the C content to be 0.14 to 0.22% and the Mn content to be 5.3 to 6.5%, so that the steel sheet can obtain the optimum hardenability and obtain a high hardness martensite structure.
Si在炼钢过程中为脱氧元素，还能够产生固溶强化作用，但含量过高时会降低韧性等性能。因此，本发明将Si含量控制为0.1～0.5％。Si is a deoxidizing element in the steel making process, and can also produce solid solution strengthening, but when the content is too high, the properties such as toughness are lowered. Therefore, the present invention controls the Si content to be 0.1 to 0.5%.
Ti在钢中形成TiN析出，能够抑制高温下奥氏体晶粒粗化，从而有利于细化马氏体组织，提高马氏体的强度及硬度。微量添加就能够发挥作用，过量添加将导致夹杂物粗大。所以，本发明将Ti含量控制为0.01～0.04％。Ti forms TiN precipitates in steel, which can suppress austenite grain coarsening at high temperatures, which is advantageous for refining the martensite structure and improving the strength and hardness of martensite. A slight addition can work, and excessive addition will result in coarse inclusions. Therefore, the present invention controls the Ti content to be 0.01 to 0.04%.
而实施例中为了制造本发明的热轧耐磨钢板，采用的方法包括下述步骤：In the embodiment, in order to manufacture the hot-rolled wear-resistant steel sheet of the present invention, the method adopted includes the following steps:
将板坯在1030～1120℃的温度条件下加热，加热时间与板坯厚度的比值为0.9～1.3min/mm；然后对加热后的板坯进行轧制，终轧温度为820～870℃，轧制的总变形量≥80％，轧制后得到钢板的厚度为4～16mm；以及将轧制后的钢板空冷至室温。The slab is heated at a temperature of 1030 to 1120 ° C, and the ratio of the heating time to the thickness of the slab is 0.9 to 1.3 min/mm; then the heated slab is rolled, and the finishing temperature is 820 to 870 ° C. The total deformation of the rolling is ≥80%, and the thickness of the steel sheet after rolling is 4 to 16 mm; and the steel sheet after rolling is air-cooled to room temperature.
其中，总变形量＝(板坯的厚度-钢板的厚度)×100％/板坯的厚度。Among them, the total deformation amount = (thickness of slab - thickness of steel plate) × 100% / thickness of slab.
该制造方法的机理是：坯料加热时得到高温奥氏体组织，同时合金元素通过扩散方式均匀化。加热温度过高或保温时间过长将导致高温奥氏体晶粒过于粗大，而加热温度过低或保温时间过短不利于合金元素均匀化，因此本发明将加热温度控制在1030～1120℃，加热时间与板坯厚度之比控制在0.9～1.3min/mm。加热后坯料进行轧制，终轧温度不低于830℃，能够使变形温度处于奥氏体相区内，而终轧温度不高于870℃，能够避免再结晶奥氏体过度粗化。轧制过程中奥氏体晶粒通过再结晶得以细化，总变形量≥80％能够保证足够的再结晶细化效果。由于钢种淬透性高，16mm及以下厚度钢板的空冷冷速达到该合金成分下马氏体相变需要的冷速(≥0.1℃/s)。因此，在轧制后的空冷过程中，奥氏体能够转变为马氏体。而钢板厚度在4mm以上时，冷却速率不至于过大，有利于马氏体组织中碳化物的析出，进一步提高组织硬度。冷却至室温后，钢板得到具有足够硬度 的马氏体组织，钢板表面布氏硬度HBW达到370～430。The mechanism of the manufacturing method is that a high temperature austenite structure is obtained when the billet is heated, and the alloy elements are homogenized by diffusion. If the heating temperature is too high or the holding time is too long, the high-temperature austenite grains will be too coarse, and the heating temperature is too low or the holding time is too short, which is not conducive to the homogenization of the alloying elements. Therefore, the heating temperature of the present invention is controlled at 1030 to 1120 ° C. The ratio of the heating time to the thickness of the slab is controlled to be 0.9 to 1.3 min/mm. After heating, the billet is rolled, and the finishing temperature is not lower than 830 ° C, so that the deformation temperature is in the austenite phase region, and the finish rolling temperature is not higher than 870 ° C, which can avoid excessive coarsening of recrystallized austenite. Austenite grains are refined by recrystallization during rolling, and a total deformation amount of ≥80% can ensure sufficient recrystallization refining effect. Due to the high hardenability of steel grades, the air cooling rate of steel plates of 16 mm and below reaches the cooling rate (≥0.1 °C/s) required for martensitic transformation under the alloy composition. Therefore, austenite can be transformed into martensite during air cooling after rolling. When the thickness of the steel plate is above 4 mm, the cooling rate is not too large, which is favorable for the precipitation of carbides in the martensite structure and further increases the hardness of the structure. After cooling to room temperature, the steel sheet obtained a martensitic structure having sufficient hardness, and the surface hardness of the steel sheet was HB-WH of 370-430.
为了对本发明做进一步详细说明，发明人提供了如下实施例。In order to further explain the present invention, the inventors provide the following examples.
实施例1：将厚度为100mm，化学成分以质量百分比计，包含0.17％C、5.7％Mn、0.22％Si、0.019％Ti，以及余量Fe和杂质元素的板坯，在1080℃的温度条件下加热110min。对加热后的坯料进行轧制，轧制规程如表1所示：Example 1: A slab having a thickness of 100 mm and a chemical composition of 0.17% C, 5.7% Mn, 0.22% Si, 0.019% Ti, and the balance Fe and impurity elements, at a temperature of 1080 ° C Heat down for 110 min. The heated billet is rolled, and the rolling schedule is as shown in Table 1:
表1 实施例1轧制规程Table 1 Example 1 rolling procedure
Figure PCTCN2018108991-appb-000001
Figure PCTCN2018108991-appb-000001
其总变形量为89.3％，终轧温度为846℃。轧制后空冷至室温。The total deformation was 89.3% and the finishing temperature was 846 °C. After rolling, it was air cooled to room temperature.
得到厚度为10.7mm的热轧耐磨钢板，化学成分以质量百分比计，包含0.17％C、5.9％Mn、0.22％Si、0.019％Ti，以及余量的Fe和杂质元素。微观组织如图1所示全为马氏体组织，检测钢板的表面布氏硬度达到409HBW。A hot-rolled wear-resistant steel sheet having a thickness of 10.7 mm was obtained, and the chemical composition contained 0.17% C, 5.9% Mn, 0.22% Si, 0.019% Ti, and the balance of Fe and impurity elements in terms of mass percentage. The microstructure is all martensite as shown in Fig. 1. The surface hardness of the steel plate is 409HBW.
实施例2：将厚度为80mm，化学成分以质量百分比计，包含0.14％C、6.5％Mn、0.1％Si、0.04％Ti，以及余量Fe和杂质元素的板坯，在1120℃的温度条件下加热72min。对加热后的坯料进行轧制，轧制规程如表2所示：Example 2: A slab having a thickness of 80 mm and a chemical composition of 0.14% C, 6.5% Mn, 0.1% Si, 0.04% Ti, and the balance Fe and impurity elements, at a temperature of 1120 ° C Heat down for 72 min. The heated billet is rolled, and the rolling schedule is as shown in Table 2:
表2 实施例2轧制规程Table 2 Example 2 rolling procedure
Figure PCTCN2018108991-appb-000002
Figure PCTCN2018108991-appb-000002
其总变形量80％，终轧温度为870℃。轧制后空冷至室温。The total deformation amount is 80%, and the finishing temperature is 870 °C. After rolling, it was air cooled to room temperature.
得到厚度为16mm的热轧耐磨钢板，化学成分以质量百分比计，包含0.14％C、6.5％Mn、0.1％Si、0.04％Ti，以及余量Fe和杂质元素。显微组织如图2所示均为马氏体组织，测得钢板的表面布氏硬度达到370HBW。A hot-rolled wear-resistant steel sheet having a thickness of 16 mm was obtained, and the chemical composition contained, by mass percentage, 0.14% C, 6.5% Mn, 0.1% Si, 0.04% Ti, and the balance Fe and impurity elements. The microstructure is shown in Figure 2 as a martensite structure, and the surface hardness of the steel plate is 370 HBW.
实施例3：将厚度为60mm，化学成分以质量百分比计，包含0.22％C、 5.3％Mn、0.5％Si、0.01％Ti，以及余量Fe和杂质元素的板坯，在1030℃的温度条件下加热78min。对加热后的坯料进行轧制，轧制规程如表3所示：Example 3: a slab having a thickness of 60 mm and a chemical composition of 0.22% C, 5.3% Mn, 0.5% Si, 0.01% Ti, and the balance Fe and impurity elements, at a temperature of 1030 ° C Heat down for 78 min. The heated billet is rolled, and the rolling schedule is as shown in Table 3:
表3 实施例3轧制规程Table 3 Example 3 rolling procedure
Figure PCTCN2018108991-appb-000003
Figure PCTCN2018108991-appb-000003
其总变形量93.3％，终轧温度为820℃。轧制后空冷至室温。The total deformation was 93.3%, and the finishing temperature was 820 °C. After rolling, it was air cooled to room temperature.
得到厚度为4mm的低成本热轧耐磨钢板，化学成分以质量百分比计，包含0.22％C、5.3％Mn、0.5％Si、0.01％Ti，以及余量Fe和杂质元素，显微组织如图3所示均为马氏体组织，检测钢板的表面布氏硬度达到430HBW。A low-cost hot-rolled wear-resistant steel plate having a thickness of 4 mm is obtained, and the chemical composition contains 0.22% C, 5.3% Mn, 0.5% Si, 0.01% Ti, and the balance Fe and impurity elements in terms of mass percentage, and the microstructure is as shown in the figure. 3 shows a martensite structure, and the surface hardness of the steel plate is 430 HBW.

Claims (7)

  1. 一种热轧耐磨钢板，其特征在于，化学成分以重量百分比计包含有：0.14～0.22％的C、5.3～6.5％的Mn、0.1～0.5％的Si、0.01～0.04％的Ti，以及余量的Fe和不可避免的杂质元素。A hot-rolled wear-resistant steel sheet characterized by comprising: 0.14 to 0.22% of C, 5.3 to 6.5% of Mn, 0.1 to 0.5% of Si, 0.01 to 0.04% of Ti, and The balance of Fe and the inevitable impurity elements.
  2. 根据权利要求1所述的热轧耐磨钢板，其特征在于，化学成分以重量百分比计包含有：0.17～0.22％的C、5.3～5.7％的Mn、0.22～0.5％的Si、0.01～0.019％的Ti，以及余量的Fe和不可避免的杂质元素。The hot-rolled wear-resistant steel sheet according to claim 1, wherein the chemical composition comprises, by weight percentage, 0.17 to 0.22% of C, 5.3 to 5.7% of Mn, 0.22 to 0.5% of Si, and 0.01 to 0.019. % Ti, as well as the balance of Fe and inevitable impurity elements.
  3. 根据权利要求1所述的热轧耐磨钢板，其特征在于，所述热轧耐磨钢板的微观组织结构为马氏体。The hot-rolled wear-resistant steel sheet according to claim 1, wherein the hot-rolled wear-resistant steel sheet has a microstructure of martensite.
  4. 根据权利要求1所述的热轧耐磨钢板，其特征在于，所述热轧耐磨钢板的厚度为4～16mm。The hot-rolled wear-resistant steel sheet according to claim 1, wherein the hot-rolled wear-resistant steel sheet has a thickness of 4 to 16 mm.
  5. 一种如权利要求1～4任一所述的热轧耐磨钢板的制造方法，其特征在于，包括下述步骤：A method of manufacturing a hot-rolled wear-resistant steel sheet according to any one of claims 1 to 4, comprising the steps of:
    (1)将板坯在1030～1120℃的温度条件下加热，加热时间与板坯厚度的比值为0.9～1.3min/mm；(1) heating the slab at a temperature of 1030 to 1120 ° C, the ratio of the heating time to the thickness of the slab is 0.9 to 1.3 min / mm;
    (2)对加热后的板坯进行轧制，终轧温度为820～870℃，轧制后得到钢板的厚度≤16mm；(2) rolling the heated slab, the final rolling temperature is 820 ~ 870 ° C, the thickness of the steel plate after rolling is ≤ 16 mm;
    (3)将轧制后的钢板空冷至室温。(3) The rolled steel sheet is air-cooled to room temperature.
  6. 根据权利要求5所述的热轧耐磨钢板的制造方法，其特征在于，所述步骤(2)中，轧制的总变形量≥80％。The method of producing a hot-rolled wear-resistant steel sheet according to claim 5, wherein in the step (2), the total deformation amount of the rolling is ≥80%.
  7. 根据权利要求5所述的热轧耐磨钢板的制造方法，其特征在于，所述步骤(2)中，轧制后得到的钢板厚度为4～16mm。The method of producing a hot-rolled wear-resistant steel sheet according to claim 5, wherein in the step (2), the steel sheet obtained after rolling has a thickness of 4 to 16 mm.
PCT/CN2018/108991 2018-02-07 2018-09-30 Hot-rolled, abrasion-resistant steel plate and manufacturing method thereof WO2019153764A1 (en)

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CN108300943B (en) * 2018-02-07 2020-06-19 南京钢铁股份有限公司 Hot-rolled wear-resistant steel plate and manufacturing method thereof
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CN105483536A (en) * 2015-12-10 2016-04-13 南京钢铁股份有限公司 Novel abrasion resistant steel plate and production method thereof
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