WO2021017520A1 - 一种表面质量优良的耐磨钢及其制备方法 - Google Patents

一种表面质量优良的耐磨钢及其制备方法 Download PDF

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WO2021017520A1
WO2021017520A1 PCT/CN2020/083992 CN2020083992W WO2021017520A1 WO 2021017520 A1 WO2021017520 A1 WO 2021017520A1 CN 2020083992 W CN2020083992 W CN 2020083992W WO 2021017520 A1 WO2021017520 A1 WO 2021017520A1
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steel plate
steel
surface quality
wear
temperature
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PCT/CN2020/083992
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English (en)
French (fr)
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刘俊
李国忠
杨洋
许晓红
武金明
苗丕峰
徐国庆
王小双
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江阴兴澄特种钢铁有限公司
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Priority to EP20846997.3A priority Critical patent/EP4006191A4/en
Priority to US17/927,878 priority patent/US20230203630A1/en
Priority to KR1020227006254A priority patent/KR102680518B1/ko
Priority to AU2020322810A priority patent/AU2020322810B2/en
Publication of WO2021017520A1 publication Critical patent/WO2021017520A1/zh

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Definitions

  • the invention relates to the technical field of iron-based alloys, in particular to a wear-resistant steel with excellent surface quality and a manufacturing method thereof.
  • Wear-resistant steel plates are widely used in key components of machinery and equipment that require high strength and good wear resistance in industries such as construction machinery, mining and transportation, and road transportation, such as excavator buckets, central troughs of scraper conveyors, and mining dump trucks. Fight and so on.
  • domestic wear-resistant steel manufacturers have done a lot of work on how to improve the comprehensive mechanical properties of steel plates.
  • the inventions of Chinese Patent Publication Nos. CN104451409A, CN103014543A, CN102747280B, and CN106521314B from surface hardness, overall hardness, high toughness, easy welding Reports have been made in various aspects.
  • the purpose of the present invention is to provide a low-alloy easily weldable wear-resistant steel with excellent surface quality and a preparation method thereof.
  • the microstructure of the low-alloy wear-resistant steel plate is fine tempered martensite; tensile strength ⁇ 1200MPa, elongation ⁇ 12%, Charpy V longitudinal impact energy at -40°C ⁇ 30J; Brinell hardness meets 360 ⁇ 460HB.
  • the surface quality of the steel plate is good, and there are no surface defects such as pores, inclusions, pits, and pressed iron oxide scale.
  • the steel plate does not need to be grinded, and the surface mottling depth caused by the peeling of the oxide scale is ⁇ 0.1mm.
  • the steel plate has good welding performance, the carbon equivalent CEV is less than 0.40; the welding crack sensitivity coefficient PCM is less than 0.25, which can realize direct welding without preheating.
  • a wear-resistant steel with excellent surface quality the chemical composition of which is C: 0.12 ⁇ 0.20%, Si: ⁇ 0.1%, Mn: 0.6-1.20%, Nb :0.010 ⁇ 0.040%, V: ⁇ 0.01%, Ti: 0.010% ⁇ 0.030, Al: ⁇ 0.04%, Ni: ⁇ 0.1%, Cu: ⁇ 0.1%, Cr: 0.10 ⁇ 0.40%, Mo: ⁇ 0.1%, B: 0.001 ⁇ 0.005%, Ca: 0.0010 ⁇ 0.0050%, P: ⁇ 0.010%, S: ⁇ 0.0015%, O: ⁇ 0.0012%, N: ⁇ 0.0035%, H: ⁇ 0.0002%, the balance is Fe and impossible Impurity elements to avoid.
  • the present invention controls the carbon equivalent CEV ⁇ 0.4; PCM ⁇ 0.25;
  • the thickness of the low-alloy easily weldable wear-resistant steel plate with excellent surface quality of the present invention is 4-20 mm.
  • Carbon is the most basic and important element in wear-resistant steel, which determines the hardness level, toughness and welding performance of the steel plate. Low carbon content, low hardness, good toughness, and excellent weldability; high carbon content, high strength, high hardness, but the steel plate has reduced plastic toughness and poor weldability. Based on the design hardness of the steel plate in the range of 360HB to 460HB, and considering the toughness and welding performance of the steel plate, the carbon content in the present invention is controlled to be 0.12 to 0.20%.
  • Si Silicon is dissolved in ferrite and austenite to improve strength and hardness. Excessive content will deteriorate the toughness of martensitic steel, increase the sensitivity of welding cracks, and reduce the surface quality.
  • This study shows that there is an important relationship between the Si content and the relatively shallow oxidation mottling on the surface of the wear-resistant steel. As shown in Figure 1, when the Si content is 0.25%, most of the secondary oxidation spots with a depth of 0.02 to 0.2 mm exist on the surface of the wear-resistant steel. When the Si content is 0.15%, after shot blasting, the mottling depth is reduced to less than 0.15mm, as shown in Figure 2.
  • Mn It strongly improves the hardenability of steel and reduces the critical cooling rate of martensite transformation.
  • the manganese content is specified to be 0.80 ⁇ 1.30%.
  • Nb It is a strong C and N compound forming element, which serves to pin austenite grain boundaries and inhibits the growth of austenite grains during heating. At the same time, the strength and toughness of steel are significantly improved through grain refinement. When the addition amount is less than 0.010%, the effect is not obvious, and when it is more than 0.040%, it is easy to segregate at the grain boundary and the toughness is reduced. Therefore, the present invention stipulates that the niobium content should be in the range of 0.010% to 0.040%.
  • Ti is a strong carbide forming element. TiC particles are fine and distributed in the grain boundaries to achieve the effect of refining the grains of the steel plate and welds, while improving the wear resistance of the steel plate. However, if the Ti content is too high, it is easy to form micron-sized liquid-separated TiN, which is detrimental to the low-temperature impact performance of the steel plate; in order to obtain better weld performance, the present invention controls the Ti content to 0.010% to 0.030%.
  • Al Refining the grain element, while ensuring the formation of fine Ti particles and ensuring the toughness of the steel plate. Too high Al content will result in the formation of too many Al 2 O 3 inclusions, which will affect the surface quality of the steel plate. At the same time, because the invention of wear-resistant steel adopts low Si design, too high Al content will affect the top slag in the steelmaking process. The reduction of SiO 2 increases the Si content in the molten steel, thereby affecting the formation of the later secondary oxide scale. Therefore, the present invention stipulates that the Al content is less than or equal to 0.04%.
  • Ni, Cu The most commonly used elements that effectively improve the low-temperature toughness of steel. However, due to the relatively high price and poor economy, the present invention eliminates the addition of Ni and Cu, which greatly improves the cost competitiveness of the invention steel.
  • the chromium content is controlled at 0.10 to 0.40%.
  • Mo An element that improves the hardenability of steel and is conducive to the formation of full martensite during quenching. However, due to the higher price and poor economy, the addition of Mo is eliminated in the present invention, which improves the cost competitiveness of the invention steel.
  • B In the present invention, 0.001-0.005% of a trace amount of B is added, and its main purpose is to improve the hardenability of the steel sheet, thereby reducing the addition of other precious metals and reducing the cost. More than 0.005% of B is likely to segregate, form borides, and seriously deteriorate the toughness of the steel sheet.
  • Ca treatment is usually used for inclusion denaturation treatment, changing the elongated inclusions such as MnS into spherical inclusions such as CaS, reducing the anisotropy of the steel plate and improving the comprehensive performance of the steel plate.
  • the invention controls the content of Ca from 0.0010% to 0.0050%.
  • P and S Harmful elements, adversely affecting the plasticity and toughness of materials.
  • the present invention pursues pure steel, reduces the influence of inclusions on the surface quality, and strictly controls the content of P ⁇ 0.01% and the content of S ⁇ 0.0015%. .
  • O, N, H harmful gas elements, high content, many inclusions, easy to produce white spots, greatly reducing the plasticity and toughness of the steel plate, affecting the welding performance, and at the same time easily forming inclusion defects on the surface of the steel plate, affecting the surface quality.
  • the invention strictly controls the content of O to not more than 0.0012%; the content of N to not more than 0.0035%; and the content of H to be less than or equal to 0.0002%.
  • the present invention also provides a method for preparing the above-mentioned low-alloy easily weldable wear-resistant steel plate with excellent surface quality.
  • the specific process is as follows:
  • Smelting process adopt converter method to smelt, control the final slag basicity R(Cao/SiO 2 ) ⁇ 3 of converter tapping, slag blocking operation, control slag per ton of steel within 3kg, effectively control the increase of Si in molten steel caused by tapping slag ;
  • the molten steel is sent to the LF refining furnace for refining, and the oxidation of the refining slag is controlled, and the FeO+MnO content in the slag is controlled to be less than 2%, SiO 2 content is less than 8%, and Al 2 O 3 content is 15% to 35%; the refining time does not exceed 1 It can prevent the molten steel from greatly increasing Si; the molten steel undergoes VD or RH vacuum treatment, the vacuum degree is ⁇ 0.5mbar, and the time is not less than 30min to reduce the generation of pores.
  • the calcium iron wire is used to replace the traditional silicon-calcium wire for Ca treatment; the inclusion
  • Continuous casting process In order to control the internal porosity and segregation of the steel plate, low superheat pouring, full argon gas protection pouring, and dynamic light reduction control are carried out.
  • the superheat of molten steel is controlled at 5-20°C, and the center segregation is not higher than C1.0.
  • Heating process Studies have shown that when the heating temperature is greater than 1180°C, Fe 2 SiO 4 reacts with FeO to produce a molten binary eutectic, which will promote the local oxidation reaction of the billet, resulting in difficulty in subsequent descaling and causing scale pressing Formation indicates defects.
  • the invention adopts a lower heating temperature, and the heating temperature of the casting slab is controlled at 1100-1180°C.
  • the time in the furnace for controlling the soaking section shall not exceed 1 hour.
  • High-pressure water descaling is performed before the steel plate is rolled, and the descaling pressure at the nozzle is controlled above 21MPa. Rough rolling and opening and high pressure descaling for the last two passes to fully remove the oxide scale once. Studies have shown that when the steel plate is above 1050°C, the high-temperature slab will rapidly produce secondary scale.
  • the present invention controls the intermediate billet head and tail temperature to be lower than 1000°C after rough rolling. In order to shorten the high temperature waiting time of the steel plate and control the uniformity of the grain size of the steel plate, the finishing rolling temperature of the present invention is controlled at ⁇ 930°C. High-pressure water descaling is used for finishing rolling. The total descaling pass of finishing rolling shall not be less than 3 passes, and the final rolling temperature is controlled at ⁇ 820°C. The steel plate does not use accelerated cooling to avoid the generation of multiple scales.
  • the steel plate must be shot blasted before heat treatment to completely remove the complete and dense oxide scale on the surface of the steel plate to avoid press-in defects in the subsequent straightening treatment.
  • Quenching (water quenching) heat treatment process the steel plate is quenched after rolling, the quenching temperature is 880 ⁇ 940°C, and the holding time after the furnace temperature reaches the temperature is 20 ⁇ 60min. To ensure the uniformity of the steel plate, the temperature control accuracy is ⁇ 10°C.
  • Tempering process The steel plate adopts low temperature tempering, and the temperature is controlled at 150 ⁇ 250°C. After the furnace temperature reaches the warmth, the holding time is 30-60min. To ensure the uniformity of the steel plate, the temperature control accuracy is ⁇ 10°C.
  • Chemical composition adopts low carbon equivalent design, steel plate CEV ⁇ 0.40; welding crack sensitivity coefficient PCM ⁇ 0.25, which can realize welding without preheating;
  • the invention adopts converter method for smelting, controls the final slag basicity R(Cao/SiO 2 ) ⁇ 3 of the converter tapping, and controls the slag blocking operation to control the slag per ton of steel within 3kg, effectively controlling the increase of Si in the molten steel caused by the tapping slag;
  • the molten steel is sent to the LF refining furnace for refining, to control the oxidation of the refining slag, and control the FeO+MnO content in the slag ⁇ 2%, SiO 2 content ⁇ 8%, Al 2 O 3 content 15% to 35%; refining time does not exceed 1 hour ,
  • control the total level of inclusions A, B, C, D ⁇ 2.5 improve the ultra-low temperature impact toughness of the steel plate, and avoid surface inclusion defects;
  • the invention adopts a lower heating temperature, and the heating temperature of the casting slab is controlled at 1100-1180°C.
  • the time in the furnace for controlling the soaking section shall not exceed 1 hour.
  • the steel plate of the invention is subjected to high-pressure water descaling before rolling, and the descaling pressure at the nozzle is controlled to be above 21 MPa.
  • the rough rolling and the last two passes are subjected to high pressure descaling to fully remove the primary oxide scale, and at the same time quickly reduce the surface temperature of the steel plate to avoid secondary oxidation; the invention controls the intermediate billet head and tail temperature to be lower than 1000°C after rough rolling.
  • the present invention In order to shorten the high temperature waiting time of the steel plate, the present invention appropriately increases the finish rolling opening temperature and controls it at ⁇ 930°C. In order to quickly reduce the rolling temperature, high-pressure water descaling is used in the finishing rolling. The total descaling passes of the finishing rolling shall not be less than 3 passes, and the final rolling temperature is controlled at ⁇ 800°C. After rolling, the steel plate does not adopt accelerated cooling such as water cooling to avoid the generation of multiple scales. Use stacking slow cooling or cover slow cooling or air cooling for cooling.
  • the steel plate must be shot blasted before heat treatment to completely remove the complete and dense oxide scale on the surface of the steel plate to avoid the occurrence of press-in defects in the subsequent quenching and tempering and steel finishing treatment.
  • the surface quality of the steel plate produced by the invention is good, and there are no surface defects such as air pockets, inclusions, pits and pressed-in oxide scale.
  • the surface mottling depth caused by the peeling of the iron oxide scale is less than or equal to 0.1mm, and the steel plate surface grinding is not required.
  • the method of the present invention can be popularized and applied to other steel plates, such as steel for high-strength marine ship plates, steel for high-rise buildings, steel for bridges, steel for engineering machinery, steel for pressure vessels, and the like.
  • Figure 1 shows the surface quality of steel plate corresponding to 0.25% Si.
  • Figure 2 shows the surface quality of the steel plate corresponding to 0.15% Si.
  • Figure 3 shows the surface quality of the steel plate corresponding to 0.05% Si.
  • Figure 4 shows the composition analysis of the oxide scale on the surface of the steel plate corresponding to 0.25% Si.
  • Figure 5 shows the surface quality of the 12mm thick steel plate of Example 1.
  • the production process of the wear-resistant steel of the present invention is: converter steelmaking -> LF refining -> VD or RH high vacuum degassing -> continuous casting -> heating -> rolling -> shot blasting -> Quenching -> Tempering.
  • Example 1-2 The present invention will be further described below in conjunction with Examples 1-2.
  • the specific chemical components of Example 1-2 are shown in Table 1. Steel plate carbon equivalent CEV ⁇ 0.4, welding crack sensitivity coefficient PCM ⁇ 0.25, welding without preheating can be realized.
  • the production method of the low-alloy easily weldable wear-resistant steel plate with excellent surface quality in embodiment 1-2 of the present invention includes the following steps:
  • step (3) Rolling: Put the continuous casting billet obtained in step (2) into a walking heating furnace, the heating temperature is between 1100 ⁇ 1180°C, and the soaking period is between 30 ⁇ 60min; the billet is descaled by high pressure water after being discharged from the furnace , The descaling pressure is 21MPa; rough rolling is carried out after treatment.
  • the first and last two passes of rough rolling are respectively subjected to high-pressure descaling (that is, the high-pressure water descaling is performed in the pass with a large reduction rate), and the temperature of the steel plate is between 930-1000°C.
  • the finishing temperature of finishing rolling is ⁇ 800°C.
  • the number of finish rolling descaling passes shall not be less than 3 times. Refer to Table 4 for specific related process parameters of rolling.
  • step (3) the steel plate obtained in step (3) is put into the shot blasting equipment for shot blasting treatment to completely remove the dense oxide scale on the surface of the steel plate.
  • Quenching + tempering After shot blasting, the steel plate is quenched. The quenching temperature is 910°C, the holding time is 40min, and the quenching medium is water. After quenching, the steel plate adopts low temperature tempering, the tempering temperature is 200°C, and the holding time is 40min.
  • Example 1-2 The performance of the steel plate corresponding to Example 1-2 is shown in Table 5. The results show that the steel plate has excellent mechanical properties, tensile strength ⁇ 1200MPa, elongation ⁇ 12%, -40°C Charpy V-shaped longitudinal impact energy ⁇ 30J; Brinell hardness all satisfy 360-460HB.
  • the surface of the steel plate of the embodiment is shown in Figure 3 and Figure 5.
  • the results show that the surface quality of the steel plate is good, there are no defects such as pores, inclusions, pits and scaly spots, no grinding treatment is required, and the surface quality is excellent.
  • the surface quality of steel plates with different Si contents is shown in Figures 1 and 2.
  • Figures 1 and 2 show the surface quality of the steel plate obtained when the Si content of the traditional wear-resistant steel is greater than 0.1%.
  • the invention reasonably designs C, Si and other alloy components and their proportions, reduces alloy costs, and reasonably designs smelting, steel rolling and heat treatment processes, so that the obtained steel plate has excellent mechanical properties and welding performance; at the same time, the surface quality of the steel plate is excellent , Provides feasibility for engineering equipment manufacturing with high standard surface quality requirements, and has advantages and prospects for mass production and application.
  • Table 1 The chemical composition of the wear-resistant steel plate of the embodiment (wt%)
  • the present invention also includes other implementation modes, and all technical solutions formed by equivalent transformations or equivalent substitutions shall fall within the protection scope of the claims of the present invention.

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Abstract

一种表面质量优良的耐磨钢，成分为C：0.12～0.20％，Si：≤0.1％，Mn：0.6～1.20％，Nb：0.010～0.040％，V：≤0.01％，Ti：0.010％～0.030，Al：≤0.04％，Ni：≤0.1％，Cu：≤0.1％，Cr：0.10～0.40％，Mo：≤0.1％，B：0.001～0.005％，Ca：0.0010～0.0050％，P：≤0.010％，S：≤0.0015％，O：≤0.0012％，N：≤0.0035％，H：≤0.0002％，余量为Fe，碳当量CEV≤0.4；PCM≤0.25。生产工艺流程为：转炉炼钢->LF精炼->VD或RH高真空脱气->连铸->加热->轧制->抛丸处理->淬火->回火。该耐磨钢具有更好的表面质量，不存在气坑、夹杂、麻坑及压入的氧化铁皮等表面缺陷。氧化铁皮脱落引起的表面花斑深度≤0.1mm，可以不进行钢板表面修磨。在元素设计的基础上进一步能够实现不预热焊接和优良的韧性。

Description

一种表面质量优良的耐磨钢及其制备方法 技术领域
本发明涉及铁基合金技术领域，具体涉及一种表面质量优良的耐磨钢及其制造方法。
背景技术
耐磨钢板广泛应用于工程机械、矿山采运、道路运输等行业要求强度高、耐磨性好的机械设备关键部件上，如挖掘机挖斗、刮板输送机中部槽、矿用自卸车车斗等等。近年来，国内耐磨钢生产企业对如何提高钢板综合力学性能进行了大量的工作，比如：中国专利公开号为CN104451409A、CN103014543A、CN102747280B、CN106521314B的发明从表面硬度、通体硬度、高韧性、易焊接等方面进行了报道。
随着工程机械设备品种的进一步开发，设备制造商对耐磨钢板表面缺陷控制提出了越来越严的要求。一方面表面缺陷会成为各种失效开裂的裂纹源；另一方面影响设备外观。钢板生产商对于表面缺陷在不影响钢板厚度的情况下，采取局部修磨进行处理，但这对后期设备表面涂漆产生较大影响，导致漆膜凹凸不平，大大影响表面质量。开发不需修磨的高表面质量易焊接耐磨钢板，是钢板生产企业急需解决的难题。
发明内容
本发明的目的在于提供一种具有优良表面质量的低合金易焊接耐磨钢及其制备方法。该低合金耐磨钢板显微组织为细小的回火马氏体；抗拉强度≥1200MPa，延伸率≥12％，-40℃夏比V型纵向冲击功≥30J；布氏硬度均满足360～460HB。钢板表面质量良好，不存在气孔、夹杂、麻坑、及压入的氧化铁皮等表面缺陷。钢板可不进行修磨，氧化铁皮脱落引起的表面花斑深度≤0.1mm。钢板焊接性能良好，碳当量CEV≤0.40；焊接裂纹敏感系数PCM≤0.25，可实现不预热直接焊接。
本发明解决上述问题所采用的技术方案为：一种表面质量优良的耐磨钢，化学成分按质量百分比计为C：0.12～0.20％，Si：≤0.1％，Mn：0.6～1.20％，Nb：0.010～0.040％，V：≤0.01％，Ti:0.010％～0.030，Al：≤0.04％，Ni：≤0.1％，Cu：≤0.1％，Cr：0.10～0.40％，Mo：≤0.1％，B：0.001～0.005％，Ca：0.0010～0.0050％，P：≤0.010％，S：≤0.0015％，O：≤0.0012％，N：≤0.0035％，H：≤0.0002％，余量为Fe及不可避免的杂质元素。
按CEV＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15式计算，其化学成分满足碳当量 CEV≤0.40；按PCM＝C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B式计算，焊接裂纹敏感系数PCM≤0.25。
为实现不预热焊接和并具有优良的韧性，本发明控制碳当量CEV≤0.4；PCM≤0.25；
本发明所述表面质量优良的低合金易焊接耐磨钢板的厚度为4～20mm。
本发明中钢成分的设置原理如下：
C：碳是耐磨钢中最基本、最重要的元素，决定了钢板的硬度级别、韧性和焊接性能。碳含量低，硬度低、韧性好、焊接性优良；碳含量高，强度高，硬度高，但钢板塑韧性降低，焊接性差。基于钢板设计硬度在360HB～460HB，考虑到钢板韧性及焊接性能，本发明中碳含量控制为0.12～0.20％。
Si：硅固溶在铁素体和奥氏体中提高强度和硬度。含量过高会恶化马氏体钢的韧性，增加焊接裂纹敏感性，同时表面质量下降。本研究表明，Si含量与耐磨钢表面较浅的氧化花斑有着重要联系。如图1所示，Si含量为0.25％时，耐磨钢表面存在大部分深度为0.02～0.2mm的二次氧化花斑。当Si含量为0.15％时，抛丸后，花斑深度降低为0.15mm以下，见图2。当Si含量降为0.05％时，钢板抛丸后，未出现表面花斑等缺陷，质量良好，见图3。研究表明，当耐磨钢中存在一定的Si含量时，氧化铁皮与基体间容易形成一定的Fe 2SiO 4化合物，该化合物增加了氧化铁皮的粘性，在除鳞过程中很难被除去，从而在轧钢过程中被压入，造成耐磨钢表面会存在浅浅的一层花斑缺陷，见图4。本研究表明，耐磨钢中当Si含量≤0.1％时，钢板表面质量良好，抛丸后不存在明显缺陷，可以满足客户高标准表面质量要求，同时也降低了钢板焊接裂纹敏感系数。因此本发明，严格控制耐磨钢Si含量≤0.1％。
Mn：强烈提高钢的淬透性，降低马氏体转变临界冷却速度。当锰的含量较低，上述作用不显著，钢板强度和韧性偏低等。过高时有使晶粒粗化的倾向，同时会引起连铸坯偏析形成MnS、韧性差和可焊性降低，故本发明中考虑到合金的综合加入，规定锰含量加入量介于0.80～1.30％的范围内。
Nb：是强烈的C、N化物的形成元素，起到对奥氏体晶界的钉扎作用，在加热时抑制奥氏体晶粒的长大。通过晶粒细化同时显著提高钢的强度和韧性。添加量小于0.010％时效果不明显，大于0.040％时易在晶界偏聚，韧性降低。因此，本发明规定铌含量应介于0.010～0.040％的范围内。
Ti：Ti是强碳化物形成元素，TiC颗粒细小，分布在晶界，达到细化钢板和焊缝晶粒的效果，同时提高钢板耐磨性。但Ti含量过高，容易形成微米级尺寸的液析TiN，对钢板的低温冲击性能不利；本发明为获得较好的焊缝性能，控制Ti含量在0.010％～0.030％。
Al：细化晶粒元素，同时可以保证细小Ti颗粒的形成，保证钢板韧性。Al含量过 高，会导致过多的Al 2O 3夹杂物的形成，影响钢板表面质量；同时，由于本耐磨钢发明采用低Si设计，Al含量过高会把炼钢过程顶渣中的SiO 2还原，增加钢水中Si的含量，从而影响后期二次氧化铁皮的形成，因此本发明规定Al含量≤0.04％。
Ni、Cu：有效提高钢的低温韧性的最常用元素。但由于价格较高，经济性较差，本发明取消Ni、Cu的加入，大大提高了发明钢种的成本竞争力。
Cr：降低马氏体转变临界冷却速度，提高淬透性。Cr过高会降低钢板的可焊接性。本发明中铬含量控制在0.10～0.40％。
Mo：提高钢淬透性的元素，有利于淬火时全马氏体的形成。但由于价格较高，经济性差，本发明中取消Mo的加入，提高发明钢种成本竞争力。
B：本发明加入0.001～0.005％的微量B，其主要目的是提高钢板的淬透性，从而减少其他贵重金属的添加量，降低成本。超过0.005％的B很容易产生偏析，形成硼化物，严重恶化钢板韧性。
Ca：Ca处理通常用来进行夹杂物变性处理，改变MnS等长条状夹杂物为CaS等球形夹杂物，降低钢板各向异性，提高钢板综合性能。本发明控制Ca含量0.0010％～0.0050％。
P和S：有害元素，对材料塑性和韧性有不利影响。本发明追求纯净钢，降低夹杂物对表面质量的影响，严格控制P含量≤0.01％，S含量≤0.0015％。。
O、N、H：有害气体元素，含量高，夹杂物多，易产生白点，大大降低钢板塑性、韧性，影响焊接性能，同时在钢板表面容易形成夹杂缺陷，影响表面质量。本发明严格控制O含量不高于0.0012％；N含量不高于0.0035％；H含量≤0.0002％。
本发明另提供上述一种具有优良表面质量的低合金易焊接耐磨钢板的制备方法，具体工艺如下，
冶炼工艺：采用转炉方式冶炼，控制转炉出钢终渣碱度R(Cao/SiO 2)≥3，挡渣操作，吨钢下渣控制在3kg以内，有效控制出钢下渣引起的钢水增Si；钢水送入LF精炼炉进行精炼，控制精炼渣氧化性，控制渣中FeO+MnO含量≤2％，SiO 2含量≤8％，Al 2O 3含量15％～35％；精炼时间不超过1小时，避免钢水大幅度增Si；钢水经过VD或RH真空处理，真空度≤0.5mbar，时间不低于30min，减少气孔的产生。本发明钢水脱气后采用钙铁线替代传统的硅钙线进行Ca处理；夹杂物控制A、B、C、D类总级别≤2.5，避免表面夹杂。
连铸工艺：为了控制钢板内部疏松、偏析，进行低过热度浇注，全程氩气保护浇注，以及动态轻压下控制。钢水过热度控制在5～20℃，中心偏析不高于C1.0级。
加热工艺：研究表明，加热温度大于1180℃时，Fe 2SiO 4与FeO发生反应，生产熔融态的二元共晶体，会促进钢坯局部的氧化反应，导致后续除鳞困难，引起氧化皮压入形成表明缺陷。本发明采用较低的加热温度，铸坯加热温度控制在1100～1180℃。控制 均热段在炉时间，不得超过1小时。
轧钢工艺：钢板轧制前进行高压水除鳞，控制喷嘴处除鳞压力在21MPa以上。粗轧开轧及最后2道次进行高压除鳞，充分去除一次氧化铁皮。研究表明，钢板在1050℃以上，高温板坯会迅速产生二次氧化铁皮，本发明控制粗轧后中间坯头尾温度低于1000℃。为缩短钢板高温待温时间，及控制钢板晶粒度均匀性，本发明精轧开轧温度控制在≥930℃。精轧开轧采用高压水除鳞，精轧总除鳞道次不得低于3道次，终轧温度控制在≥820℃。钢板不采用加速冷却，避免多次氧化铁皮的产生。
表面处理：钢板在热处理前必须进行抛丸处理，完全去除钢板表面完整致密的氧化皮，避免后续矫直处理中的压入缺陷产生。
淬火(水淬)热处理工艺：轧制后钢板进行淬火处理，淬火温度880～940℃，炉温到温后保温时间为20～60min。为保证钢板的均匀性，温度控制精度为±10℃。
回火工艺：钢板采用低温回火，温度控制在150～250℃。炉温到温后保温时间为30～60min。为保证钢板的均匀性，温度控制精度为±10℃。
本发明与现有耐磨钢生产技术相比：
化学成分设计中取消Si、Mo元素的加入，降低了钢板的合金成本，控制Si含量≤0.1％，避免了Fe 2SiO 4化合物在耐磨钢基体与氧化铁皮界面形成，导致钢板表面质量下降；同时降低了钢板焊接裂纹敏感性；
化学成分采用低碳当量设计，钢板CEV≤0.40；焊接裂纹敏感系数PCM≤0.25，可实现不预热焊接；
本发明采用转炉方式冶炼，控制转炉出钢终渣碱度R(Cao/SiO 2)≥3，挡渣操作，吨钢下渣控制在3kg以内，有效控制出钢下渣引起的钢水增Si；钢水送入LF精炼炉进行精炼，控制精炼渣氧化性，控制渣中FeO+MnO含量≤2％，SiO 2含量≤8％，Al 2O 3含量15％～35％；精炼时间不超过1小时，避免钢水大幅度增Si；夹杂物控制A、B、C、D类总级别≤2.5，提高钢板超低温冲击韧性的同时，避免表面夹杂缺陷；
本发明采用较低的加热温度，铸坯加热温度控制在1100～1180℃。控制均热段在炉时间，不得超过1小时。
本发明钢板轧制前进行高压水除鳞，控制喷嘴处除鳞压力在21MPa以上。粗轧开轧及最后2道次进行高压除鳞，充分去除一次氧化铁皮，同时快速降低钢板表面温度，避免二次氧化；本发明控制粗轧后中间坯头尾温度低于1000℃，。
为缩短钢板高温待温时间，本发明适当提高精轧开轧温度，控制在≥930℃。为快速降低轧制温度，精轧开轧采用高压水除鳞，精轧总除鳞道次不得低于3道次，终轧温度控制在≥800℃。轧后钢板不采用加速冷却如水冷，避免多次氧化铁皮的产生。采用堆垛缓冷或加罩缓冷或空冷进行降温。
钢板在热处理前必须进行抛丸处理，完全去除钢板表面完整致密的氧化皮，避免后 续调质及钢板精整处理中的压入缺陷产生。
本发明生产钢板表面质量良好，不存在气坑、夹杂、麻坑及压入的氧化铁皮等表面缺陷。氧化铁皮脱落引起的表面花斑深度≤0.1mm，可以不进行钢板表面修磨。
本发明方法，可以推广应用至其它钢板，如高强海工船板用钢、高层建筑用钢、桥梁用钢、工程机械用钢、压力容器用钢等。
附图说明
图1是0.25％Si对应钢板的表面质量。
图2是0.15％Si对应钢板的表面质量。
图3是0.05％Si对应钢板的表面质量。
图4是0.25％Si对应钢板表面氧化铁皮组分分析。
图5是实施例1的12mm厚的钢板表面质量。
具体实施方式
以下结合实施例对本发明作进一步详细描述。
以钢板为例，本发明耐磨钢的生产工艺流程为：转炉炼钢->LF精炼->VD或RH高真空脱气->连铸->加热->轧制->抛丸处理->淬火->回火。
下面结合实施例1-2对本发明做进一步说明。实施例1-2具体化学成分见表1。钢板碳当量CEV≤0.4，焊接裂纹敏感系数PCM≤0.25，可实现不预热焊接。
本发明实施例1-2的具有优良表面质量的低合金易焊接耐磨钢板的生产方法，包括如下步骤：
(1)冶炼：采用150吨转炉冶炼，转炉终渣碱度R(Cao/SiO 2)≥3.0；转炉出钢，每吨钢下渣量≤2kg；转炉冶炼具体工艺参数见表2；钢水进入LF炉精炼，控制精炼终渣(FeO+MnO)≤2.0％；SiO 2含量≤8％；Al 2O 3含量15％～35％；精炼时间30～60min；精炼钢水进入RH脱气，压力0.5mbar，，时间30～50min。精炼具体工艺参数见表3。
(2)连铸：将冶炼的钢水浇铸成150mm厚的连铸坯。浇铸温度控制在液相线以上5-20℃。浇铸过程中实施动态轻压下，板材低倍控制在C0.5～C1.0。
(3)轧制：将步骤(2)所得连铸坯放入步进式加热炉，加热温度介于1100～1180℃，均热段时间介于30～60min；钢坯出炉后经高压水除鳞，除鳞压力21MPa；处理后进行粗轧。粗轧开轧第一及最后2道次分别进行高压除鳞(即在大压下率的道次匹配高压水除鳞)，钢板待温温度介于930—1000℃。精轧终轧温度≥800℃。精轧除鳞道次不得低于3次。轧制具体相关工艺参数见表4。
(4)抛丸处理：将步骤(3)所得钢板进入抛丸设备进行抛丸处理，完全去除钢板表面致密氧化皮。
(5)淬火+回火：抛丸后钢板进行淬火处理，，淬火温度为910℃，保温时间为40min，淬火介质为水。淬火后，钢板采用低温回火，回火温度200℃，保温时间为40min。
实施例1-2对应的钢板性能见表5。结果表明，钢板力学性能优良，抗拉强度≥1200MPa，延伸率≥12％，-40℃夏比V型纵向冲击功≥30J；布氏硬度均满足360～460HB。
实施例钢板表面见图3、图5。结果表明，钢板表面质量良好，不存在气孔、夹杂、麻坑及氧化皮花斑等缺陷，无需修磨处理，表面质量极好。作为对比，不同Si含量的钢板表面质量如图1、2所示。图1和2为传统耐磨钢Si含量大于0.1％情况下获得的钢板表面质量。
本发明合理设计了C、Si等合金成分及其配比，降低了合金成本，并合理设计了冶炼、轧钢和热处理工艺，使获得的钢板具有优良的力学性能和焊接性能；同时钢板表面质量优异，为具有高标准表面质量要求的工程设备制造提供了可行性，具有批量生产及应用的优势和前景。
表1实施例耐磨钢板的化学成分(wt％)
Figure PCTCN2020083992-appb-000001
表2实施例转炉冶炼工艺参数表
Figure PCTCN2020083992-appb-000002
表3实施例精炼工艺参数表
Figure PCTCN2020083992-appb-000003
表4轧制工艺控制
Figure PCTCN2020083992-appb-000004
表5本发明实施例力学性能
Figure PCTCN2020083992-appb-000005
除上述实施例外，本发明还包括有其他实施方式，凡采用等同变换或者等效替换方式形成的技术方案，均应落入本发明权利要求的保护范围之内。

Claims (10)

  1. 一种表面质量优良的耐磨钢，其特征在于：化学成分按质量百分比计为C：0.12～0.20％，Si：≤0.1％，Mn：0.6～1.20％，Nb：0.010～0.040％，V：≤0.01％，Ti:0.010％～0.030，Al：≤0.04％，Ni：≤0.1％，Cu：≤0.1％，Cr：0.10～0.40％，Mo：≤0.1％，B：0.001～0.005％，Ca：0.0010～0.0050％，P：≤0.010％，S：≤0.0015％，O：≤0.0012％，N：≤0.0035％，H：≤0.0002％，余量为Fe及不可避免的杂质元素。
  2. 根据权利要求1所述的表面质量优良的耐磨钢，其特征在于：按CEV＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15式计算，其化学成分满足碳当量CEV≤0.40；按PCM＝C+Si/30+(Mn+Cu+Cr)/20+Ni/60+Mo/15+V/10+5B式计算，焊接裂纹敏感系数PCM≤0.25。
  3. 根据根据权利要求1所述的表面质量优良的耐磨钢，其特征在于：当产品形式为钢板时，钢板的厚度为4～20mm。
  4. 根据权利要求1或2或3所述的表面质量优良的耐磨钢，其特征在于：钢板表面质量良好，不存在气孔、夹杂、麻坑、及压入的氧化铁皮等表面缺陷；钢板可不进行修磨，氧化铁皮脱落引起的表面花斑深度≤0.1mm。
  5. 根据权利要求1或2或3所述的表面质量优良的耐磨钢，其特征在于：抗拉强度≥1200MPa，延伸率≥12％，-40℃夏比V型纵向冲击功≥30J；布氏硬度满足360～460HB。
  6. 一种表面质量优良的耐磨钢的制备方法，其特征在于，包括如下步骤：
    (1)冶炼
    采用转炉方式冶炼，控制转炉出钢终渣碱度R(Cao/SiO 2)≥3，挡渣操作，吨钢下渣控制≤3kg；钢水送入LF精炼炉进行精炼，控制渣中FeO+MnO含量≤2％，SiO 2含量≤8％，Al 2O 3含量15％～35％；精炼时间≤1小时；钢水经过VD或RH真空处理，真空度≤0.5mbar，时间不低于30min；采用钙铁线替代传统的硅钙线进行Ca处理；夹杂物控制A、B、C、D类总级别≤2.5；
    (2)连铸
    采用低过热度、全程氩气保护浇注，以及动态轻压下控制；
    (3)加热轧制
    采用较低的铸坯加热温度：控制在1100～1180℃；控制铸坯均热段在炉时间不得超过1小时；
    钢板轧制前进行高压水除鳞，粗轧开轧及最后2道次分别再除鳞；控制粗轧后中间坯头尾温度≤1000℃；提高精轧开轧温度使≥930℃；为快速降低轧制温度，精轧开轧前采用高压水除鳞，精轧期间总除鳞道次不得低于3道次，终轧温度控制在≥800℃； 轧后钢板严禁加速冷却；
    (4)抛丸处理
    钢板在热处理前必须进行抛丸处理，去除钢板表面完整致密的氧化皮；
    (5)调制处理
    钢板淬火处理，淬火温度880～940℃，炉温到温后保温时间为20～60min；钢板低温回火，回火温度150～250℃，炉温到温后保温时间为30～60min。
  7. 根据权利要求6所述的表面质量优良的耐磨钢的制备方法，其特征在于：步骤(3)中，钢水过热度控制在5～20℃，中心偏析不高于C1.0级。
  8. 根据权利要求6所述的表面质量优良的耐磨钢的制备方法，其特征在于：步骤(4)中，高压水除鳞时，喷嘴处除鳞压力≥21MPa。
  9. 根据权利要求6所述的表面质量优良的耐磨钢的制备方法，其特征在于：步骤(5)淬火和回火的温度控制精度为±10℃。
  10. 根据权利要求6所述的表面质量优良的耐磨钢的制备方法，其特征在于：步骤(3)轧后钢板严禁水冷，采用堆垛缓冷或加罩缓冷或空冷进行降温。
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CN114410894B (zh) * 2021-12-28 2023-08-22 舞阳钢铁有限责任公司 一种减少12Cr2Mo1VR钢淬火裂纹的方法
CN114737116A (zh) * 2022-03-30 2022-07-12 鞍钢股份有限公司 一种700MPa级耐磨损腐蚀钢及其制造方法
CN115094331A (zh) * 2022-07-18 2022-09-23 柳州钢铁股份有限公司 一种低成本的q690钢板及其生产方法
CN115505852A (zh) * 2022-10-26 2022-12-23 河北普阳钢铁有限公司 一种耐蚀农机用钢材及其制造方法

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