高強高韌性耐磨鋼板的沖擊磨料磨損性能研究
發(fā)布時間：2018-08-02 09:23
【摘要】：磨損是材料失效的主要形式之一。80%上的機械材料消耗于磨損,上的裝備惡性事故起因于過渡的磨損和潤滑失效。因此,開發(fā)高性能的耐磨鋼鐵材料,對減少材料磨損過程中的損失、提高機械裝備的使用壽命有著至關(guān)重要的意義。低合金耐磨鋼板作為一種重要的耐磨鋼鐵材料,合金含量低、綜合性能良好、生產(chǎn)靈活方便及價格便宜等持點,被廣泛的應(yīng)用于工程機械、礦山機械及冶金機械等設(shè)備的生產(chǎn)制造。本文主要以Cr-Ni-Mo、Mo-Ti-B高強韌性馬氏體鋼、不同形變強化的高氮奧氏體鋼為研究對象,通過對實驗材料最大變形區(qū)域垂直切表面金相組織、顯微硬度與磨損面的SEM、TEM組織及EBSD大小角晶界取向分布特征等進行研究,綜合討論了材料強化硬化及磨損失效機理。(1)對Cr-Ni-Mo、Mo-Ti-B馬氏體鋼進行沖擊磨損實驗,并對磨損亞表面硬化程度進行表征。結(jié)果表明:隨著沖擊時間的增加,在2.5J的沖擊功作用下,Mo-Ti-B鋼耐磨性逐步下降,在3.5J的沖擊功作用下,Cr-Ni-Mo鋼耐磨性比Mo-Ti-B鋼的耐磨性要好。在低中沖擊載荷作用下,Cr-Ni-Mo鋼在較硬硬質(zhì)磨料(白剛玉)磨損量較大,而在高沖擊載荷下其磨損量相當(dāng)。亞表層的硬度明顯高于基體的硬度,隨亞表層深度增加,加工硬化程度逐漸降低。(2)通過對材料基體以及2.5J沖擊時間為2h的沖擊磨損試驗EBSD研究分析,實驗結(jié)果表明:Cr-Ni-Mo鋼的大小角度晶界沖擊前后分別63.6%、36.4%,47.4%、52.6%;Mo-Ti-B鋼的大小角度晶界沖擊前后分別59.1%、40.9%,61.2%、38.8%。Cr-Ni-Mo鋼小角度密度晶界提高導(dǎo)致材料強度不斷提高,使材料的耐磨性提高。而Mo-Ti-B鋼的大小角度晶界變化不明顯。(3)在3.5J沖擊功作用下,Cr-Ni-Mo鋼耐磨性呈現(xiàn)先降低后增加的趨勢,對亞表面最大變形區(qū)進行SEM、TEM觀察,實驗結(jié)果表明:基體組織呈現(xiàn)低溫回火特性,馬氏體組織逐步分解成為鐵素體基體以及大量的尺寸在500nm的硬質(zhì)碳化物,通過TEM衍射花樣標(biāo)定,析出相為ε-碳化物,碳化物在基體組織中起到骨架支撐作用,減少基體與磨料之間的接觸,從而提高材料的耐磨性能。而Mo-Ti-B鋼在2.5J沖擊功,沖擊2h時,在磨損表面區(qū)域馬氏體基體快速分解為鐵素體與滲碳體,隨著磨損時間的進一步增加,碳化物不斷的長大,與基體脫離共格關(guān)系,碳化物與基體之間連接薄弱,有利于微裂紋的形成,降低材料的耐磨性。(4)針對不同形變強化的高氮奧氏體鋼的沖擊磨損硬化機制進行討論,主要從切表面的顯微硬度變化,金相組織的變化,以及磨損面的磨損形貌等方面討論。研究結(jié)果表明:在1.5J、2.5J、3.5J沖擊載荷后,10mm高氮鋼亞表面硬化范圍在438.45HV～497.09HV,硬化深度在1400μm左右;而50mm高氮鋼412HV～494HV硬化深度在1000μm左右。隨著沖擊能量的提高加工硬化程度得到提升,切削痕、犁溝變少疲勞剝落坑變多。EBSD統(tǒng)計結(jié)果表明:10mm高氮鋼經(jīng)過3.5J沖擊載荷后,10mm高氮鋼小角度晶界由59.4%增加到73.7%,50mm高氮鋼小角度晶界由68.6%增加到73.6%,通過位錯纏結(jié)起到位錯強化或晶界強化作用,耐磨性均有提升的趨勢。50mm高氮鋼基體大角度晶界所占比例相對于10mm高氮鋼減小,材料的韌性有所降低。
[Abstract]:Wear is one of the main forms of material failure. The mechanical material on.80% is consumed by wear and wear. The malignant accident on the equipment is due to the transition wear and lubrication failure. Therefore, the development of high performance wear-resistant steel materials is of vital importance to reducing the loss of material wear and improving the service life of mechanical equipment. As an important wear-resistant steel material, the wear-resistant steel plate is widely used in the production of engineering machinery, mining machinery and metallurgical machinery, such as low alloy content, good comprehensive performance, convenient production and cheap price and so on. This paper mainly uses Cr-Ni-Mo, Mo-Ti-B high strength and toughness martensitic steel, and high nitrogen with different deformation intensification. Austenitic steel is the research object. Through the study of the microstructure of the vertical cutting surface in the maximum deformation area of the experimental material, the microhardness and the wear surface SEM, TEM structure and the distribution characteristics of the grain boundary orientation distribution of the EBSD size angle, the mechanism of material hardening and wear failure is discussed comprehensively. (1) the impact wear on Cr-Ni-Mo and Mo-Ti-B martensitic steel is carried out. The results showed that with the increase of impact time, the wear resistance of Mo-Ti-B steel decreased gradually with the impact time of 2.5J, and the wear resistance of Cr-Ni-Mo steel was better than that of Mo-Ti-B steel under the impact of 3.5J. Under the impact of low medium impact load, Cr-Ni-Mo steel was hard and hard abrasive. The wear amount of white corundum is larger, and its wear amount is equal under high impact load. The hardness of subsurface is obviously higher than that of matrix, and the degree of work hardening gradually decreases with the increase of subsurface depth. (2) the analysis of the impact wear of the material matrix and the impact time of 2.5J is 2H. The experimental results show that the large Cr-Ni-Mo steel is large. The small angle grain boundary before and after impact is 63.6%, 36.4%, 47.4%, 52.6% respectively. The grain boundary of Mo-Ti-B steel is 59.1%, 40.9%, 61.2%, and the grain boundary of 38.8%.Cr-Ni-Mo steel is increased to increase the material strength and improve the wear resistance of the material, and the grain boundary of the Mo-Ti-B steel is not obvious. (3) the impact work of 3.5J is made. In use, the wear resistance of Cr-Ni-Mo steel appears to be reduced first and then increased, and the maximum deformation area of the subsurface is SEM and TEM. The experimental results show that the matrix microstructure presents low temperature tempering, martensitic structure gradually decomposes into ferrite matrix and a large number of hard carbides in 500nm, demarcated by TEM diffraction pattern and precipitated. For the epsilon carbide, carbides play a skeleton support in the matrix structure, reducing the contact between the matrix and the abrasive, thus improving the wear resistance of the material. While the Mo-Ti-B steel has the impact work of 2.5J and the impact of 2h, the martensitic matrix is rapidly decomposed into ferrite and carburized body in the martensitic matrix on the worn surface, and with the further increase of the wear time, carbonization is made. The relationship between the substrate and the matrix is constantly growing, and the connection between the carbide and the matrix is weak. It is beneficial to the formation of micro cracks and the wear resistance of the material. (4) the impact and wear hardening mechanism of the high nitrogen austenite steel with different deformation intensification is discussed, mainly from the change of microhardness of the surface of the cutting surface, the change of metallographic structure, and the wear and tear. The results show that the subsurface hardening range of 10mm high nitrogen steel is in the range of 438.45HV to 497.09HV and the hardening depth is about 1400 mu m after the impact load of 1.5J, 2.5J and 3.5J, while the hardened depth of 50mm high nitrogen steel 412HV to 494HV is about 1000 mu m. With the increase of the impact energy, the hardening degree of the high nitrogen steel is improved and the cutting marks are improved. The.EBSD statistical results show that the low angle grain boundary of high nitrogen steel in 10mm is increased from 59.4% to 73.7% after 3.5J impact load, and the small angle grain boundary of 50mm high nitrogen steel increases from 68.6% to 73.6%. The effect of dislocation strengthening or grain boundary intensification through dislocation entanglement, the tendency of wear resistance to enhance.50mm high nitrogen The proportion of large angle grain boundary of steel matrix decreases with the decrease of 10mm high nitrogen steel, and the toughness of material decreases.
【學(xué)位授予單位】：昆明理工大學(xué)
【學(xué)位級別】：碩士
【學(xué)位授予年份】：2017
【分類號】：TG142.1
本文編號：2158982
[Abstract]:Wear is one of the main forms of material failure. The mechanical material on.80% is consumed by wear and wear. The malignant accident on the equipment is due to the transition wear and lubrication failure. Therefore, the development of high performance wear-resistant steel materials is of vital importance to reducing the loss of material wear and improving the service life of mechanical equipment. As an important wear-resistant steel material, the wear-resistant steel plate is widely used in the production of engineering machinery, mining machinery and metallurgical machinery, such as low alloy content, good comprehensive performance, convenient production and cheap price and so on. This paper mainly uses Cr-Ni-Mo, Mo-Ti-B high strength and toughness martensitic steel, and high nitrogen with different deformation intensification. Austenitic steel is the research object. Through the study of the microstructure of the vertical cutting surface in the maximum deformation area of the experimental material, the microhardness and the wear surface SEM, TEM structure and the distribution characteristics of the grain boundary orientation distribution of the EBSD size angle, the mechanism of material hardening and wear failure is discussed comprehensively. (1) the impact wear on Cr-Ni-Mo and Mo-Ti-B martensitic steel is carried out. The results showed that with the increase of impact time, the wear resistance of Mo-Ti-B steel decreased gradually with the impact time of 2.5J, and the wear resistance of Cr-Ni-Mo steel was better than that of Mo-Ti-B steel under the impact of 3.5J. Under the impact of low medium impact load, Cr-Ni-Mo steel was hard and hard abrasive. The wear amount of white corundum is larger, and its wear amount is equal under high impact load. The hardness of subsurface is obviously higher than that of matrix, and the degree of work hardening gradually decreases with the increase of subsurface depth. (2) the analysis of the impact wear of the material matrix and the impact time of 2.5J is 2H. The experimental results show that the large Cr-Ni-Mo steel is large. The small angle grain boundary before and after impact is 63.6%, 36.4%, 47.4%, 52.6% respectively. The grain boundary of Mo-Ti-B steel is 59.1%, 40.9%, 61.2%, and the grain boundary of 38.8%.Cr-Ni-Mo steel is increased to increase the material strength and improve the wear resistance of the material, and the grain boundary of the Mo-Ti-B steel is not obvious. (3) the impact work of 3.5J is made. In use, the wear resistance of Cr-Ni-Mo steel appears to be reduced first and then increased, and the maximum deformation area of the subsurface is SEM and TEM. The experimental results show that the matrix microstructure presents low temperature tempering, martensitic structure gradually decomposes into ferrite matrix and a large number of hard carbides in 500nm, demarcated by TEM diffraction pattern and precipitated. For the epsilon carbide, carbides play a skeleton support in the matrix structure, reducing the contact between the matrix and the abrasive, thus improving the wear resistance of the material. While the Mo-Ti-B steel has the impact work of 2.5J and the impact of 2h, the martensitic matrix is rapidly decomposed into ferrite and carburized body in the martensitic matrix on the worn surface, and with the further increase of the wear time, carbonization is made. The relationship between the substrate and the matrix is constantly growing, and the connection between the carbide and the matrix is weak. It is beneficial to the formation of micro cracks and the wear resistance of the material. (4) the impact and wear hardening mechanism of the high nitrogen austenite steel with different deformation intensification is discussed, mainly from the change of microhardness of the surface of the cutting surface, the change of metallographic structure, and the wear and tear. The results show that the subsurface hardening range of 10mm high nitrogen steel is in the range of 438.45HV to 497.09HV and the hardening depth is about 1400 mu m after the impact load of 1.5J, 2.5J and 3.5J, while the hardened depth of 50mm high nitrogen steel 412HV to 494HV is about 1000 mu m. With the increase of the impact energy, the hardening degree of the high nitrogen steel is improved and the cutting marks are improved. The.EBSD statistical results show that the low angle grain boundary of high nitrogen steel in 10mm is increased from 59.4% to 73.7% after 3.5J impact load, and the small angle grain boundary of 50mm high nitrogen steel increases from 68.6% to 73.6%. The effect of dislocation strengthening or grain boundary intensification through dislocation entanglement, the tendency of wear resistance to enhance.50mm high nitrogen The proportion of large angle grain boundary of steel matrix decreases with the decrease of 10mm high nitrogen steel, and the toughness of material decreases.
【學(xué)位授予單位】：昆明理工大學(xué)
【學(xué)位級別】：碩士
【學(xué)位授予年份】：2017
【分類號】：TG142.1
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