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WO2022152158A1 - 一种高强韧易切削非调质圆钢及其制造方法 - Google Patents

一种高强韧易切削非调质圆钢及其制造方法 Download PDF

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Publication number
WO2022152158A1
WO2022152158A1 PCT/CN2022/071570 CN2022071570W WO2022152158A1 WO 2022152158 A1 WO2022152158 A1 WO 2022152158A1 CN 2022071570 W CN2022071570 W CN 2022071570W WO 2022152158 A1 WO2022152158 A1 WO 2022152158A1
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quenched
round steel
steel
tempered
tempered round
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PCT/CN2022/071570
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English (en)
French (fr)
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高加强
赵四新
黄宗泽
陈林
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宝山钢铁股份有限公司
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Priority to EP22739036.6A priority Critical patent/EP4261320A4/en
Priority to KR1020237022934A priority patent/KR20230116043A/ko
Priority to AU2022208884A priority patent/AU2022208884A1/en
Priority to JP2023541685A priority patent/JP2024503015A/ja
Priority to US18/271,172 priority patent/US20240052470A1/en
Publication of WO2022152158A1 publication Critical patent/WO2022152158A1/zh
Priority to ZA2023/07142A priority patent/ZA202307142B/en

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    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to a steel material and a manufacturing method thereof, in particular to a high-strength and toughness free-cutting non-quenched and tempered steel and a manufacturing method thereof.
  • High-strength steel bars are usually used to manufacture high-safety mechanical and structural components, such as auto parts or key stress components of construction machinery. Therefore, high-strength steel not only needs to have high strength, but also has properties such as high strength, toughness, and easy cutting.
  • an appropriate chemical composition is usually selected, and a quenching + tempering heat treatment or a controlled rolling + controlled cooling process is used to produce high-strength steel.
  • the quenching + tempering process is used to produce high-strength steel
  • the content of alloying elements, especially carbon elements can be optimized so that the steel can form a martensite structure during the cooling process, thereby improving the hardenability of the steel.
  • This kind of high-strength steel mainly composed of martensite has a high dislocation density, which will lead to poor impact toughness of the steel, and if there are small defects such as micro-cracks during the stretching process, it will quickly fracture and fail, resulting in a relatively high fracture toughness of the steel. Low.
  • Traditional non-quenched and tempered steel usually refers to adding micro-alloying elements such as vanadium on the basis of medium and low carbon steel, and through controlled rolling (forging) and controlled cooling, fine carbonitrides are dispersed and precipitated in ferrite + pearlite, Thereby a strengthening effect is produced, so that the steel can obtain mechanical properties equivalent to those after quenching and tempering without quenching and tempering after rolling (after forging).
  • the new non-quenched and tempered steels of the bainitic and martensitic types have higher strengths than conventional non-quenched and tempered steels.
  • the toughness of martensitic non-quenched and tempered steel is relatively low, while bainitic non-quenched steel can achieve the strength and toughness of alloy structural steel after quenching and tempering. It is a development direction of high-strength and tough non-quenched and tempered steel. , optimizing the process and other means to obtain fine-grained or bainite structure.
  • Non-quenched and tempered steel has good economy and certain strength and toughness, and can be widely used in fields such as automobiles and construction machinery, which is an inevitable trend of future development.
  • the non-quenched and tempered steel in the prior art still has the problem that the strength and hardness are sufficient but the toughness is insufficient.
  • One of the objectives of the present invention is to provide a high-strength and toughness free-cutting non-quenched and tempered round steel, which not only has good impact toughness and plasticity, but also has good fatigue resistance, which is easy to cut , which can meet the performance requirements of steel in application scenarios such as automobiles and construction machinery.
  • the present invention provides a kind of high-strength and toughness free-cutting non-quenched and tempered round steel, in terms of mass percentage, the content of each chemical element is:
  • a non-quenched and tempered round steel with good impact toughness, plasticity and fatigue resistance and easy to cut can be obtained.
  • microalloying elements such as vanadium, niobium, and aluminum are added, and the microalloying of the elements is used to improve the precipitation and precipitation strengthening effect of the microalloying elements, thereby refining the grains of the microstructure of the round steel.
  • sulfur element is added to the steel to improve the cutting performance of the non-quenched and tempered round steel of the present invention.
  • C element can improve the hardenability of steel, so that the steel can form a phase transformation structure with higher hardness in the process of quenching and cooling.
  • the content of C element in the steel increases, the proportion of the hard phase will increase, and the hardness of the steel will be increased, but at the same time, the toughness of the steel will be reduced; and when the content of the C element in the steel is too low, it will lead to the phase transformation structure of the steel such as If the bainite content is too low, the steel cannot obtain sufficient tensile strength. Therefore, in the non-quenched and tempered round steel of the present invention, the mass percentage content of element C is controlled between 0.36% and 0.45%.
  • Si element is beneficial to improve the strength of steel, and adding an appropriate amount of Si can avoid the formation of coarse carbides when the steel is tempered.
  • the content of Si element in the steel should not be too high.
  • the mass percentage content of Si element can be controlled between 0.20% and 0.70%.
  • Mn is one of the main elements affecting the hardenability of steel.
  • Mn mainly exists in the form of solid solution in steel, which can effectively improve the hardenability of steel, and form a high-strength low-temperature transformation structure during quenching, which makes the steel have good strength and toughness.
  • the content of Mn in the steel should not be too high. When the content of Mn in the steel is too high, it will lead to the formation of more retained austenite, reduce the yield strength of the steel, and easily lead to central segregation.
  • the mass percentage content of the Mn element is controlled between 1.25% and 1.85%.
  • Cr element can significantly improve the hardenability of steel. Adding an appropriate amount of Cr element to the steel can effectively form a hardened bainite structure, thereby improving the strength of the steel. Correspondingly, the content of Cr element in steel should not be too high. When the content of Cr element in steel is too high, coarse carbides will be formed and the impact performance of steel will be reduced. In the non-quenched and tempered round steel of the present invention, the mass percentage content of Cr element is controlled between 0.15-0.55%.
  • Ni exists in the form of solid solution in steel, and adding an appropriate amount of Ni element to steel can effectively improve the low temperature impact performance of the material.
  • the content of Ni element in the steel should not be too high. Too high Ni content will lead to too high content of retained austenite in the steel, thereby reducing the strength of the steel.
  • the mass percentage content of Ni element is controlled between 0.10% and 0.25%.
  • Mo element can be solid solution in steel, and is beneficial to improve the hardenability of steel and improve the strength of steel. However, considering the cost of the precious alloy Mo element, in order to effectively control the cost of the alloy, the content of Mo element in the steel should not be too high. In the non-quenched and tempered round steel of the present invention, the mass percentage content of Mo element is controlled between 0.10 and 0.25%.
  • Al element can form fine precipitates with N, thereby pinning the grain boundaries and inhibiting the growth of austenite grains.
  • the content of Al element in the steel should not be too high. Too high content of Al will lead to the formation of larger oxides, and coarse hard inclusions will reduce the impact toughness and fatigue properties of the steel.
  • the mass percentage content of Al element is controlled between 0.02-0.05%.
  • Nb The addition of Nb element to steel can form fine precipitates, which can inhibit the recrystallization of steel and effectively refine the grains. Grain refinement plays an important role in improving the mechanical properties of steel, especially strength and toughness. At the same time, grain refinement also helps to reduce the hydrogen embrittlement susceptibility of steel. However, the content of Nb element in the steel should not be too high. When the Nb content in the steel is too high, coarse NbC particles will be formed during the smelting process, which will reduce the impact toughness of the steel. Therefore, in the non-quenched and tempered round steel of the present invention, the mass percentage of Nb element is controlled at
  • V is an important alloying element for the strengthening of non-quenched and tempered steels.
  • V element can form precipitates with C element or N element, resulting in precipitation strengthening, and can pin grain boundaries, refine grains, and improve the strength of steel.
  • the content of element V in the steel should not be too high. If the content of element V in the steel is too high, coarse VC particles will be formed, which will reduce the impact toughness of the steel. Therefore, in the non-quenched and tempered round steel of the present invention, the mass percentage of V element is controlled between 0.10 and 0.25%.
  • S element can form sulfide inclusions with Mn element, thereby improving the cutting performance of steel.
  • the mass percentage content of S element is controlled between 0.02 and 0.06%.
  • non-quenched and tempered round steel of the present invention also contains Cu, and the content of Cu in terms of mass percentage is: 0 ⁇ Cu ⁇ 0.25%.
  • Cu can improve the strength of steel, and is beneficial to improve the weather resistance and corrosion resistance of steel.
  • the content of Cu element in the steel should not be too high. If the content of Cu in the steel is too high, it will be enriched in the grain boundary during the heating process, resulting in the weakening of the grain boundary and the cracking. Therefore, in the non-quenched and tempered round steel of the present invention, the mass percentage of Cu can be controlled to be 0 ⁇ Cu ⁇ 0.25%.
  • the content of each chemical element satisfies at least one of the following items in terms of mass percentage: P ⁇ 0.015%; N ⁇ 0.015%; O ⁇ 0.002%; Ti ⁇ 0.003 %; Ca ⁇ 0.005%.
  • P, N, O, Ti and Ca are all impurity elements in steel. If technical conditions allow, in order to obtain steel with better performance and better quality, impurity elements in steel should be reduced as much as possible content.
  • P is easy to segregate at the grain boundary in the steel, which will reduce the bonding energy of the grain boundary and deteriorate the impact toughness of the steel. Therefore, the mass percentage content of P in the non-modulated round steel of the present invention can be controlled as follows: P ⁇ 0.015%.
  • N is an interstitial atom, which can form nitrides or carbonitrides in steel, that is, MX-type precipitates, which play the role of precipitation strengthening and refinement strengthening.
  • MX-type precipitates which play the role of precipitation strengthening and refinement strengthening.
  • an excessively high N content will form coarse particles, which cannot achieve the effect of refining the grains, because N is enriched at the grain boundaries and defects as interstitial atoms, resulting in a decrease in the impact toughness of the steel.
  • the mass percentage content of N can be controlled as follows: N ⁇ 0.015%.
  • O can form oxides and composite oxides with the Al element in the steel. In order to ensure the uniformity of the steel structure and make the low-temperature impact energy and fatigue properties meet the requirements, in the non-quenched and tempered round steel of the present invention, it can be The mass percentage content of O is controlled as follows: O ⁇ 0.002%.
  • Ti can form fine precipitates in steel.
  • the mass percentage content of Ti can be controlled as follows: Ti ⁇ 0.003%.
  • Ca element can improve the size and morphology of sulfide inclusions in steel, but Ca element easily forms coarse inclusions and affects the fatigue properties of the final product.
  • the mass percentage content of Ca can be controlled as follows: Ca ⁇ 0.005%.
  • the value of the hardenability critical ideal diameter DI of the above-mentioned non-quenched and tempered round steel is 5.0 to 9.0; wherein, the hardenability critical ideal diameter DI is calculated as follows:
  • DI 0.54*C*(5.10*Mn-1.12)*(0.70*Si+1)*(0.363*Ni+1)*(2.16*Cr+1)*(3.00*Mo+1)*(0.365*Cu +1)*(1.73*V+1)
  • the range of the microalloying element coefficient r M/N of the above-mentioned non-quenched and tempered round steel is 1.1 to 9.9; wherein, the microalloying coefficient r M/N is calculated as follows:
  • the microalloying element coefficient r M/N is used to describe the fine dispersion degree of the MX (X refers to C or N) precipitation phase.
  • X refers to C or N
  • Al, Nb and V can all form the MX microalloying precipitation phase, which can refine the microalloying phase.
  • it is easy to form coarse precipitates and reduce the impact toughness and fatigue life of the steel; if the coefficient of microalloying elements is too small, Then a suitable amount of fine precipitates will not be formed, and the effect of refining the bainite grains will not be achieved.
  • the carbon equivalent Ceq of the above non-quenched and tempered round steel is 0.60-1.0%; wherein, the carbon equivalent Ceq is calculated as follows:
  • the lower limit of the carbon equivalent Ceq needs to be limited to 0.60%.
  • the upper limit of the carbon equivalent Ceq is made 1.0%.
  • the carbon equivalent in the non-quenched and tempered round steel of the present invention is controlled between 0.60-1.0%, and the specific value can be adjusted according to actual needs to meet the use requirements of the non-quenched and tempered round steel of the present invention in different occasions.
  • the non-quenched and tempered round steel of the present invention is a non-quenched and tempered steel with a bainite matrix, that is, the microstructure of the non-quenched and tempered round steel includes bainite, and in any of the above non-quenched and tempered round steels On the cross-section, the area of bainite accounts for more than 85% of the cross-sectional area.
  • the bainite transformation temperature T B of the non-quenched and tempered round steel of the present invention is 515-565°C; wherein, the bainite transformation temperature T B is calculated as follows, and the unit is °C:
  • T B 830-270*C-90*Mn-37*Ni-70*Cr-83*Mo
  • the steel is cooled to a temperature equal to or less than the bainite transformation temperature T B , so that a bainite structure is formed in the steel.
  • microstructure of the above non-quenched and tempered round steel also includes retained austenite, and at least one of ferrite or pearlite.
  • non-quenched and tempered round steel has tensile strength Rm ⁇ 1000MPa, elongation A ⁇ 12%, area shrinkage Z ⁇ 35%, and Charpy impact energy Aku ⁇ 27J .
  • the present invention also provides a method for manufacturing non-quenched and tempered round steel, comprising the steps of:
  • the smelting can be made by electric furnace smelting or converter smelting, and is subjected to refining and vacuum treatment.
  • a vacuum induction furnace can also be used for smelting.
  • the casting can be die casting or continuous casting.
  • the heating temperature is controlled to be 1050-1250° C.
  • the holding time is 3-24 h, so as to ensure that the non-quenched and tempered steel of the present invention is completely austenitized during the heating process.
  • the final rolling temperature or the final forging temperature is controlled to be ⁇ 800°C, and the cooling is performed after rolling or forging.
  • the forging can be directly forged to the final product size; rolling can either directly roll the billet to the final product size, or use the billet to first roll to the specified intermediate billet size, and then perform intermediate heating and rolling. to the final finished size.
  • the intermediate heating temperature of the intermediate blank can be controlled between 1050 and 1250° C.
  • the holding time can be controlled between 3 and 24 hours.
  • the cooling after rolling or forging is slow cooling, generally the cooling rate is ⁇ 1.5°C/s, and the cooling method can be air cooling or air cooling.
  • the finishing step may include peeling and heat treatment of the round steel, and non-destructive testing for quality assurance.
  • the peeling process performed as needed may be turning peeling or grinding wheel peeling, etc.
  • the heat treatment process performed as needed may be annealing or isothermal annealing, etc.
  • the non-destructive testing performed as needed may be ultrasonic testing or magnetic particle testing.
  • the high-strength and tough free-cutting non-quenched and tempered round steel and the manufacturing method thereof have the following beneficial effects:
  • the present invention develops a non-quenched and tempered steel with high strength and toughness and excellent cutting performance by rationally designing the chemical composition and combining with the optimized process.
  • the non-quenched and tempered steel has a bainite-based structure and is There are dispersed and distributed fine precipitates in the intenite matrix, so that the non-quenched and tempered steel of the present invention has good plasticity and toughness, and is easy to be machined.
  • the non-quenched and tempered round steel of the present invention has a reasonable manufacturing process design and a loose process window, which can realize batch commercial production on the bar production line, and be used in occasions requiring high-strength bars such as automobile crankshafts and shaft parts.
  • the non-quenched and tempered round steel of the present invention not only has good impact toughness and plasticity, but also has good fatigue resistance and is easy to cut. ⁇ 35%, Charpy impact energy A ku ⁇ 27J, which can meet the needs of applications such as automobiles and construction machinery that require high-strength and tough steel.
  • Fig. 1 is the microstructure metallographic photograph of the section of the non-quenched and tempered round steel of Example 2 under a 500-fold optical microscope;
  • Example 2 is a microstructure metallographic photograph of a section of a crankshaft prepared from the non-quenched and tempered round steel of Example 2 under a 500-fold optical microscope.
  • S1 Smelting and casting according to the chemical compositions shown in Table 1-1 and Table 1-2 below: 50kg vacuum induction furnace or 150kg vacuum induction furnace can be used for smelting, or electric furnace smelting + out-of-furnace refining + Smelting by vacuum degassing.
  • Heating control the heating temperature to be 1050-1250°C, and the holding time to be 3-24h.
  • Forging or rolling control the final rolling temperature or the final forging temperature ⁇ 800°C; cool after rolling or forging, control the cooling rate ⁇ 1.5°C/s, and the cooling method can be air cooling or air cooling.
  • Example 1 Smelting was carried out on a 50kg vacuum induction furnace according to the chemical compositions shown in Table 1-1 and Table 1-2 below.
  • the molten steel is cast into ingots, heated and forged to open billets.
  • the heating temperature is 1050 °C, and the forging is carried out after holding for 3 hours.
  • the final forging temperature is controlled to 910 °C, and finally forged into a bar with a diameter of 60mm, which is air-cooled after forging.
  • Example 2 Smelting was carried out on a 150kg vacuum induction furnace according to the chemical compositions shown in Table 1-1 and Table 1-2 below.
  • the molten steel is cast into ingots, heated and forged to open billets.
  • the heating temperature is 1100°C.
  • After 4 hours of heat preservation, the forging is carried out. Peel to ⁇ 90mm.
  • Example 3 Electric furnace smelting according to the chemical composition shown in Table 1-1 and Table 1-2, and LF refining and VD vacuum treatment, and then cast into a 320mm ⁇ 425mm continuous casting billet, and the continuous casting billet is controlled first in the preheating section Heat to 600°C, then continue to heat to 980°C in the first heating section, continue to heat to 1200°C in the second heating section after heat preservation, enter the soaking section after heat preservation for 8 hours, the temperature of the soaking section is 1220 °C, and carry out after heat preservation for 4 hours. subsequent rolling.
  • Example 4 Electric furnace smelting according to the chemical composition shown in Table 1-1 and Table 1-2, and LF refining and VD vacuum treatment, and then cast into 280mm ⁇ 280mm continuous casting billet, control the continuous casting billet first in the preheating section Heat to 620°C, then continue to heat to 950°C in the first heating section, continue to heat to 1150°C in the second heating section after heat preservation, enter the soaking section after heat preservation for 6 hours, the temperature of the soaking section is 1200 °C, and carry out after heat preservation for 2 hours. subsequent rolling.
  • Example 5 Electric furnace smelting according to the chemical composition shown in Table 1-1 and Table 1-2, and LF refining and VD vacuum treatment, and then cast into 320mm ⁇ 425mm continuous casting billet, control the continuous casting billet first in the preheating section Heat to 600°C, then continue to heat to 950°C in the first heating section, continue to heat to 1200°C in the second heating section after heat preservation, enter the soaking section after heat preservation for 8 hours, the temperature of the soaking section is 1230 °C, and follow-up after heat preservation rolling.
  • the billet is rolled out of the heating furnace after being descaled by high-pressure water, and rolled into an intermediate billet.
  • the first final rolling temperature is controlled to be 1050°C
  • the size of the intermediate billet is 220mm ⁇ 220mm, and air-cooled after rolling.
  • the preheating section of the intermediate billet is heated to 680 °C
  • the first heating section is heated to 1050 °C
  • the second heating section is heated to 1200 °C.
  • Example 6 Electric furnace smelting according to the chemical composition shown in Table 1-1 and Table 1-2, and refining and vacuum treatment, and then casting into a 280mm ⁇ 280mm continuous casting billet. 680°C, then continue to heat to 900°C in the first heating section, continue to heat to 1180°C in the second heating section after heat preservation, enter the soaking section after heat preservation for 6 hours, the temperature of the soaking section is 1200 °C, and carry out subsequent rolling after heat preservation .
  • the billet is rolled out of the heating furnace after being descaled by high-pressure water, and rolled into an intermediate billet.
  • the intermediate blank is preheated to 700°C, the first heating section is heated to 1100°C, the second heating section is heated to 1220°C, and then enters the soaking section after holding for 5 hours.
  • the soaking temperature is 1220°C.
  • Start rolling, control the second finish rolling temperature to be 920°C, and the finished bar specification is ⁇ 30mm. Air-cooled after rolling, then turned and peeled, and tested by ultrasonic flaw detection and magnetic particle flaw detection.
  • Comparative Example 1 The implementation is the same as that of Example 1, smelted in electric furnace according to the chemical composition shown in Table 1-1 and Table 1-2, and carried out refining and vacuum treatment, and then continuously cast into a billet of 280mm ⁇ 280mm, controlled continuous casting
  • the billet is first heated to 600°C in the preheating section, then heated to 980°C in the first heating section, and heated to 1200°C in the second heating section after heat preservation. , followed by rolling after heat preservation.
  • Comparative Example 2 The implementation is the same as that of Example 2, and smelting is carried out on a 150kg vacuum induction furnace according to the chemical compositions shown in Table 1-1 and Table 1-2.
  • the molten steel is cast into ingots, heated and forged to open billets.
  • the heating temperature is 1100 °C, and the forging is carried out after holding for 4 hours.
  • Comparative Example 3 The implementation is the same as that of Example 4. It is smelted in an electric furnace according to the chemical composition shown in Table 1-1 and Table 1-2, and is refined and vacuum treated, and then continuously cast into a billet of 280mm ⁇ 280mm, and the continuous casting is controlled. The billet is first heated to 680°C in the preheating section, then continues to be heated to 900°C in the first heating section, continues to be heated to 1180°C in the second heating section after heat preservation, and then enters the soaking section after heat preservation, and the temperature of the soaking section is 1200 °C , followed by rolling after heat preservation.
  • Comparative Example 4 The implementation is the same as that of Example 5. It is smelted in an electric furnace according to the chemical composition shown in Table 1-1 and Table 1-2, and is refined and vacuum treated, and then cast into a continuous casting slab of 320mm ⁇ 425mm, and the continuous casting is controlled.
  • the billet is heated to 600°C in the preheating section, then continues to be heated to 950°C in the first heating section, continues to be heated to 1200°C in the second heating section after heat preservation, enters the soaking section after heat preservation, and the temperature of the soaking section is 1230 °C, Subsequent rolling is carried out after heat preservation.
  • the billet is rolled out of the heating furnace after being descaled by high-pressure water, and rolled into an intermediate billet.
  • the preheating section of the intermediate billet is heated to 680 °C
  • the first heating section is heated to 1050 °C
  • the second heating section is heated to 1200 °C.
  • Table 1-1 lists the mass percentage ratios of each chemical element of the high-strength and tough free-cutting non-quenched and tempered round steels of Examples 1-6 and the comparative steels of Comparative Examples 1-4.
  • Table 1-2 lists the critical ideal diameter of hardenability calculated from the mass percentage content of each chemical element of the high-strength and tough free-cutting non-quenched and tempered round steel of Example 1-6 and the comparative steel of Comparative Example 1-4 DI, carbon equivalent Ceq, microalloying coefficient r M/N , bainite transformation temperature T B .
  • Example 3 5.4 5.2 0.78 548
  • Example 4 5.8 3.9 0.74 558
  • Example 5 6.3 5.5 0.78 563
  • Example 6 8.8 9.9 0.84 519
  • Comparative Example 1 9.1 6.2 0.83 524
  • Comparative Example 2 4.3 4.1 0.72 566
  • Comparative Example 3 6.7 3.8 0.80 538 Comparative Example 4 5.1 3.4 0.85 507
  • Table 2 lists the specific process parameters used in the manufacturing methods of the non-quenched and tempered round steels of Examples 1-6 and the comparative steels of Comparative Examples 1-4.
  • Example 6 in the rolling process, the steel billet is first rolled to the size of the intermediate billet specified respectively, and then heated and rolled again to Final finished size.
  • the non-quenched and tempered round steel is cut with an ordinary lathe, and the chips are collected to evaluate the cutting performance of the steel: the granular chips that are easy to break are evaluated as "good", while the continuous spiral chips that are not easy to break are evaluated as “poor”. A chip in the intervening "C" shape was evaluated as "medium”.
  • the test results of the mechanical properties and cutting properties of the obtained examples and comparative examples are listed in Table 3.
  • Table 3 lists the test results of the high-strength and tough free-cutting non-quenched and tempered round steels of Examples 1-6 and the comparative steels of Comparative Examples 1-2.
  • the three comparative examples all have parameters that do not meet the requirements of the design specification of the present invention in the chemical element composition design process. Therefore, compared with the non-quenched and tempered round steels of Examples 1-6, the strengths of the comparative steels of Comparative Examples 2 and 3 are relatively low, while the toughness of the comparative steels of Comparative Example 4 is low, and the comparative examples 3 and The use effect of Example 4 is not good.
  • the impact energy of the crankshaft prepared in Comparative Example 3 is as low as 23J.
  • the crankshaft prepared in Comparative Example 4 is not easy to break chips during the cutting process, resulting in low processing efficiency and cannot meet the requirements of use.
  • FIG. 1 is a metallographic photograph of the microstructure of the non-quenched and tempered round steel of Example 2 under a 500-fold optical microscope.
  • Example 2 the microstructure of the non-quenched and tempered round steel of Example 2 is dominated by bainite, and the area percentage of bainite on the cross-section of the round steel is ⁇ 85%.
  • the microstructure of the non-quenched and tempered round steel also has retained austenite and a small amount of ferrite + pearlite.
  • Example 2 is a microstructure metallographic photograph of a section of a crankshaft prepared from the non-quenched and tempered round steel of Example 2 under a 500-fold optical microscope.

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Abstract

本发明公开了一种高强韧易切削非调质圆钢，以质量百分比计，各化学元素的含量为：C：0.36～0.45％、Si：0.20～0.70％、Mn：1.25～1.85％、Cr：0.15～0.55％、Ni：0.10～0.25％、Mo：0.10～0.25％、Al：0.02～0.05％、Nb：0.001～0.040％、V：0.10～0.25％、S：0.02～0.06％；余量为Fe及不可避免的杂质。本发明还公开了一种非调质圆钢的制造方法，包括步骤：S1：冶炼和浇铸；S2：加热；S3：锻造或轧制；S4：精整。上述高强韧易切削非调质圆钢具有较高的强度和良好的冲击韧性、延伸率及断面收缩率，并有良好的切削性能和抗疲劳性能，可用于汽车及工程机械等需要高强度钢材的场合。

Description

一种高强韧易切削非调质圆钢及其制造方法 技术领域
本发明涉及一种钢材及其制造方法，尤其涉及一种高强韧易切削非调质钢及其制造方法。
背景技术
高强度钢棒材通常用于制造高安全性机械及结构类部件，例如：汽车零部件或工程机械的关键受力部件。因此，高强度钢不仅需要具有较高的强度，还应具有高强韧易切削等性能。
在现有技术中，通常选取适当的化学成分，并配合采用淬火+回火热处理或控制轧制+控制冷却工艺，生产高强度钢材。其中，采用淬火+回火工艺生产高强度钢材时，可以通过优化合金元素特别是碳元素的含量，以使钢在冷却过程中形成马氏体组织，从而提高钢的淬透性。这种以马氏体为主的高强度钢材位错密度大，会导致钢材冲击韧性较差，而且在拉伸过程中如果出现微小缺陷如微裂纹等会迅速断裂失效，导致钢的断裂韧性较低。
采用控轧控冷的方式生产高强度钢材，虽然无需进行淬火+回火的调质处理，即可以获得非调质钢，但由于在轧制和冷却过程中工艺控制的难度较大，因此这种生产方法会影响钢力学性能的整体均匀性。
自20世纪70年代的石油危机以来，在节能环保的推动下，德国和日本等国相继在微合金化技术的基础上，开发了49MnVS3、46MnVS6、C70S6、38MnVS6和30MnVS6等若干非调质钢，并取得了较为广泛的应用。中国在1990年代也开发了F45MnV、F35MnVN等钢种，于1995年首次发布了GB/T 15712《非调质机械结构钢》的国家标准，并于2008年进行了修订，增加到10个牌号的系列钢种。
传统的非调质钢通常指在中低碳钢的基础上添加微合金化元素如钒等，通过控轧(锻)控冷，在铁素体+珠光体中弥散析出细小的碳氮化物，从而产生强化效果，使钢在轧后(锻后)不经调质处理即可获得与调质后相当的力学性能。贝氏体和马氏体型的新型非调质钢具有比传统非调质钢更高的强度。马氏体非调质钢的韧性相对较低，而贝 氏体非调钢可以达到合金结构钢调质后的强度和韧性，是高强韧非调质钢的一个发展方向，一般采用调整化学成分、优化工艺等手段来获得细晶或贝氏体组织。
非调质钢具有良好的经济性和一定的强韧性，能广泛应用于汽车和工程机械等领域，是未来发展的必然趋势。但是，现有技术中的非调质钢仍然存在强度、硬度有余而韧性不足的问题。
发明内容
本发明的目的之一在于提供一种高强韧易切削非调质圆钢，该高强韧易切削非调质圆钢不仅具有良好的冲击韧性和塑性，还具有良好的抗疲劳性能，其易于切削，可以满足汽车和工程机械等应用场景对钢材性能的要求。
为了实现上述目的，本发明提供了一种高强韧易切削非调质圆钢，以质量百分比计，各化学元素的含量为：
C：0.36～0.45％、Si：0.20～0.70％、Mn：1.25～1.85％、Cr：0.15～0.55％、Ni：0.10～0.25％、Mo：0.10～0.25％、Al：0.02～0.05％、Nb：0.001～0.040％、V：0.10～0.25％、S：0.02～0.06％；余量为Fe及不可避免的杂质。
在本发明的技术方案中，通过合理的化学元素成分设计，可以获得具有良好的冲击韧性、塑性和抗疲劳性能，且易于切削的非调质圆钢。在本发明中，添加了钒、铌、铝等微合金元素，利用元素复合的微合金化，来提高微合金元素的沉淀析出强化效果，从而细化圆钢微观组织的晶粒。另外，钢中还加入一定量的硫元素，以提高本发明的非调质圆钢的切削性能。
本发明的非调质圆钢中，各化学元素的设计原理具体如下：
C：C元素可以提高钢材的淬透性，使钢在淬火冷却过程中形成硬度较高的相变组织。当钢中C元素含量提高时，会提高硬质相比例，提高钢材的硬度，但同时会导致钢材的韧性下降；而当钢中C元素含量太低时，则会导致钢材的相变组织如贝氏体含量过低，钢材无法获得足够的抗拉强度。因此，在本发明的非调质圆钢中，将C元素的质量百分含量控制在0.36～0.45％之间。
Si：Si元素有益于提升钢材的强度，添加适量的Si可以在钢回火时可避免形成粗大的碳化物。但需要注意的是，钢中Si元素含量不宜过高，钢中Si元素含量过高时，会降低钢材的冲击韧性。在本发明的非调质圆钢中，可以将Si元素的质量百分含量控制在0.20～0.70％之间。
Mn：Mn是影响钢淬透性的主要元素之一。Mn在钢中主要以固溶形式存在，其可以有效提高钢的淬透性，在淬火时形成高强度的低温相变组织，使得钢材具有良好的强韧性。但需要注意的是，钢中Mn元素含量不宜过高，当钢中Mn元素含量过高时，会导致形成较多的残余奥氏体，降低钢的屈服强度，并容易导致中心偏析。在本发明的非调质圆钢中，将Mn元素的质量百分含量控制在1.25～1.85％之间。
Cr：Cr元素可以显著提高钢的淬透性。钢中添加适量的Cr元素可以有效形成硬化的贝氏体组织，从而提高钢材的强度。相应地，钢中Cr元素含量不宜过高，当钢中Cr元素含量过高时，会形成粗大的碳化物，降低钢材的冲击性能。在本发明的非调质圆钢中，将Cr元素的质量百分含量控制在0.15～0.55％之间。
Ni：Ni在钢中以固溶形式存在，钢中添加适量的Ni元素可以有效提高材料的低温冲击性能。但钢中Ni元素含量不宜过高，过高的Ni含量会导致钢材中的残余奥氏体含量过高，从而降低钢材的强度。在本发明的非调质圆钢中，将Ni元素的质量百分含量控制在0.10～0.25％之间。
Mo：Mo元素可在钢中固溶，并有利于提高钢的淬透性，提高钢材的强度。但是，考虑到贵重合金Mo元素的成本，为有效控制合金的成本，钢中Mo元素含量不宜过高。在本发明的非调质圆钢中，将Mo元素的质量百分含量控制在0.10～0.25％之间。
Al：Al元素可以与N形成细小的析出物，从而实现钉扎晶界，抑制奥氏体晶粒长大。但需要注意的是，钢中Al元素含量不宜过高，过高含量的Al会导致较大的氧化物形成，而粗大的硬质夹杂会降低钢的冲击韧性和疲劳性能。在本发明的非调质圆钢中，将Al元素的质量百分含量控制在0.02～0.05％之间。
Nb：Nb元素加入钢中，能够形成细小的析出相，从而起到对钢再结晶的抑制作用，可以有效细化晶粒。晶粒细化在提高钢的力学性能尤其是强度和韧性方面有重要的作用，同时，晶粒细化还有助于降低钢的氢脆敏感性。但钢中Nb元素含量不宜过高，当钢中Nb含量过高时，在冶炼过程中会形成粗大的NbC颗粒，反而降低钢材的冲击韧性。因此，在本发明的非调质圆钢中，将Nb元素的质量百分比控制在
0.001～0.040％之间。
V：V是非调质钢强化的重要合金元素。在钢中V元素可以与C元素或N元素形成析出物，从而产生沉淀强化，并可钉扎晶界，细化晶粒，提高钢材的强度。相应地，钢中V元素含量不宜过高，若钢中V元素含量过高，则会形成粗大的VC颗粒，会降低钢材的冲击韧性。因此，在本发明的非调质圆钢中，将V元素的质量百分比控制在 0.10～0.25％之间。
S：S元素可以与Mn元素形成硫化物夹杂，从而改善钢材切削性能。但需要注意的是，钢中S元素含量过高时，不仅不利于热加工，而且还会降低钢材抗冲击性能。因此，在本发明的非调质圆钢中，将S元素的质量百分含量控制在0.02～0.06％之间。
进一步地，本发明的非调质圆钢中还含有Cu，以质量百分比计，Cu的含量为：0＜Cu≤0.25％。
Cu可以提高钢材的强度，并有利于提高钢材的耐候性及耐腐蚀能力。钢中Cu元素含量不宜过高，如果钢中Cu含量过高，则在加热过程中会富集在晶界，导致晶界弱化以致开裂。因此，在本发明的非调质圆钢中，可以将Cu的质量百分比控制为0＜Cu≤0.25％。
进一步地，在上述不可避免的杂质中，以质量百分比计，各化学元素的含量满足下述各项中的至少一项：P≤0.015％；N≤0.015％；O≤0.002％；Ti≤0.003％；Ca≤0.005％。
在上述技术方案中，P、N、O、Ti和Ca均为钢中的杂质元素，在技术条件允许情况下，为了获得性能更好且质量更优的钢材，应尽可能降低钢中杂质元素的含量。
P：P容易在钢中晶界处偏聚，会降低晶界结合能，恶化钢的冲击韧性，因此可以控制本发明非调制圆钢中P的质量百分含量为：P≤0.015％。
N：N为间隙原子，可以在钢中形成氮化物或碳氮化物，即MX型析出物，起到沉淀强化和细化强化的作用。但过高的N含量会形成粗大的颗粒，起不到细化晶粒的作用，因为N作为间隙原子在晶界及缺陷处富集，导致钢的冲击韧性降低。为了避免N元素在钢中富集，在本发明的非调质圆钢中，可以控制N的质量百分含量为：N≤0.015％。
O：O能够与钢中的Al元素形成氧化物以及复合氧化物等，为保证钢的组织均匀性并且使其低温冲击功及疲劳性能满足要求，在本发明的非调质圆钢中，可以控制O的质量百分含量为：O≤0.002％。
Ti：Ti在钢中可以形成细小析出相，钢中Ti元素含量过高时，会在冶炼过程中会形成粗大的带棱角的TiN颗粒，降低钢材的冲击韧性。因此，在本发明的非调质圆钢中，可以控制Ti的质量百分含量为：Ti≤0.003％。
Ca：Ca元素可以改善钢中硫化物夹杂的尺寸和形貌，但Ca元素容易形成粗大夹杂物而影响最终产品的疲劳性能。在本发明的非调质圆钢中，可以控制Ca的质量百分含量为：Ca≤0.005％。
进一步地，上述非调质圆钢的淬透性临界理想直径DI的值为5.0～9.0；其中，淬透性临界理想直径DI按下式计算，
DI＝0.54*C*(5.10*Mn-1.12)*(0.70*Si+1)*(0.363*Ni+1)*(2.16*Cr+1)*(3.00*Mo+1)*(0.365*Cu+1)*(1.73*V+1)
上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
在上述技术方案中，当DI值低于5.0时，钢材淬透性不足；而当DI值高于9.0时，制造困难且成本较高。
进一步地，上述非调质圆钢的微合金元素系数r M/N的范围为1.1～9.9；其中，微合金系数r M/N按下式计算，
r M/N＝([Al]/2+[Nb]/7+[V]/4)/[N]
上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
本发明中，用微合金元素系数r M/N用来描述MX(X指C或N)析出相的细小弥散程度，Al、Nb和V均能形成MX微合金析出相，起到细化贝氏体晶粒和保持晶粒尺寸稳定的作用，微合金元素系数过大，则容易在圆钢制备过程中形成粗大的析出相，降低钢的冲击韧性和疲劳寿命；微合金元素系数过小，则不会形成数量适宜的细小析出相，起不到细化贝氏体晶粒的作用。
进一步地，上述非调质圆钢的碳当量Ceq为0.60～1.0％；其中，碳当量Ceq按下式计算：
Ceq＝[C]+[Mn]/6+([Cr]+[Mo]+[V])/5+([Ni]+[Cu])/15
上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
在本发明中，若C含量低，则难以满足圆钢的强度要求，因此需要将碳当量Ceq的下限定为0.60％，另一方面，碳当量Ceq过高时，会导致钢的韧性降低，因此，将碳当量Ceq的上限设为1.0％。本发明的非调质圆钢中的碳当量控制在0.60～1.0％之间，具体值可以根据实际需要调整，以满足本发明的非调质圆钢在不同场合的使用需求。
进一步地，本发明的非调质圆钢是一种具有贝氏体基体的非调质钢，即非调质圆钢的微观组织包括贝氏体，且在上述非调质圆钢的任一截面上，贝氏体的面积占截面面积的85％以上。
进一步地，本发明的非调质圆钢的贝氏体转变温度T B为515～565℃；其中，贝氏体转变温度T B按下式计算，单位为℃：
T B＝830-270*C-90*Mn-37*Ni-70*Cr-83*Mo
上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
在圆钢制造过程中，将钢材冷却至等于或者小于贝氏体转变温度T B，使钢材内形成贝氏体组织。
进一步地，上述非调质圆钢的微观组织还包括残余奥氏体，以及，铁素体或珠光体中的至少一种。
进一步地，上述非调质圆钢的抗拉强度Rm≥1000MPa，延伸率A≥12％，断面收缩率Z≥35％，夏比冲击功A ku≥27J。
另一方面，本发明还提供了一种非调质圆钢的制造方法，包括步骤：
S1：冶炼和浇铸；
S2：加热；
S3：锻造或轧制；
S4：精整；
上述非调质圆钢的化学组分，以质量百分比计，为：
C：0.36～0.45％、Si：0.20～0.70％、Mn：1.25～1.85％、Cr：0.15～0.55％、Ni：0.10～0.25％、Mo：0.10～0.25％、Al：0.02～0.05％、Nb：0.001～0.040％、V：0.10～0.25％、S：0.02～0.06％；余量为Fe及不可避免的杂质。
在上述步骤S1中，冶炼可以采用电炉冶炼或转炉冶炼，并经过精炼及真空处理。当然在一些其他的实施方式中，也可以采用真空感应炉进行冶炼。冶炼完成后需要进行浇铸，在上述步骤S1中，浇铸可以采用模铸或连铸。
进一步地，在上述步骤S2中，控制加热温度为1050～1250℃，保温时间为3～24h，以确保使本发明的非调质钢在加热过程中完全奥氏体化。
进一步地，在上述步骤S3中，控制终轧温度或终锻温度≥800℃，轧后或锻后冷却。此外，在步骤S3中，锻造可以直接锻造至最终成品尺寸；轧制既可以采用钢坯直接轧制到最终成品尺寸，也可以采用钢坯先轧制到指定的中间坯尺寸，再进行中间加热和轧制到最终成品尺寸。其中，中间坯的中间加热温度可以控制在1050～1250℃之间，保温时间可以控制在3～24h之间。轧制或锻造后的冷却为缓慢冷却，一般冷却速度≤1.5℃/s，冷却方式可以为空冷或风冷。
在上述步骤S4中，精整步骤可以包括圆钢剥皮和热处理以及为了保证质量所进行的无损探伤等。具体地，根据需要进行的剥皮工序可以是车削剥皮或砂轮剥皮等； 根据需要进行的热处理工序可以是退火或等温退火等；根据需要进行的无损探伤可以是超声波探伤或磁粉探伤等。
本发明的高强韧易切削非调质圆钢及其制造方法相较于现有技术具有如下所述的有益效果：
1、本发明通过合理设计化学成分并结合优化工艺，开发出了一种具有高强韧性且切削性能优异的非调质钢，该非调质钢具有以贝氏体为主的组织，并且在贝氏体基体中有弥散分布的细小析出物，使本发明的非调质钢具有良好的塑性和韧性，易于切削加工。
2、本发明非调质圆钢的制造工艺设计合理，工艺窗口宽松，可以在棒材产线上实现批量商业化生产，并用于汽车曲轴和轴类零部件等需要高强度棒材的场合。
3、本发明的非调质圆钢不仅具有良好的冲击韧性和塑性，还具有良好的抗疲劳性能，易于切削，其抗拉强度R m≥1000MPa，延伸率A≥12％，断面收缩率Z≥35％，夏比冲击功A ku≥27J，能够满足汽车和工程机械等需要高强韧钢材的场合的使用需求。
附图说明
图1为实施例2的非调质圆钢的截面在500倍光学显微镜下的微观组织金相照片；
图2为由实施例2的非调质圆钢制备得到的曲轴的截面在500倍光学显微镜下的微观组织金相照片。
具体实施方式
以下由特定的具体实施例说明本发明的实施方式，本领域技术人员可由本说明书所揭示的内容轻易地了解本发明的其他优点及功效。虽然本发明的描述将结合较佳实施例一起介绍，但这并不代表此发明的特征仅限于该实施方式。恰恰相反，结合实施方式作发明介绍的目的是为了覆盖基于本发明的权利要求而有可能延伸出的其它选择或改造。为了提供对本发明的深度了解，以下描述中将包含许多具体的细节。本发明也可以不使用这些细节实施。此外，为了避免混乱或模糊本发明的重点，有些具体细节将在描述中被省略。需要说明的是，在不冲突的情况下，本发明中的实施例及实施例中的特征可以相互组合。
实施例1-6和对比例1-4
实施例1-6的高强韧易切削非调质圆钢均采用以下步骤制得：
S1：按照下述表1-1和表1-2所示的化学成分进行冶炼和浇铸：其中冶炼可以采用50kg真空感应炉或150kg真空感应炉进行冶炼，也可以采用电炉冶炼+炉外精炼+真空脱气的方式进行冶炼。
S2：加热：控制加热温度为1050～1250℃，保温时间为3～24h。
S3：锻造或轧制：控制终轧温度或终锻温度≥800℃；轧后或锻后冷却，控制冷却速度≤1.5℃/s，冷却方式可以为空冷、风冷。
S4：精整，例如剥皮。
需要说明的是，在上述S3中，当进行锻造时，直接锻造至最终成品尺寸；而当进行轧制时，既可以采用钢坯直接轧制到最终成品尺寸，也可以采用钢坯先轧制到指定的中间坯尺寸，再进行中间加热和轧制到最终成品尺寸。
其中，实施例1-6的非调质圆钢和对比例1-4的对比钢的具体工艺过程如下：
实施例1：按照下述表1-1和表1-2所示的化学成分在50kg真空感应炉上进行冶炼。钢水浇铸成钢锭，加热并经锻造开坯，加热温度1050℃，保温3h后进行锻造，控制终锻温度为910℃，最终锻造成直径Φ为60mm的棒料，锻后空冷。
实施例2：按照下述表1-1和表1-2所示的化学成分在150kg真空感应炉上进行冶炼。钢水浇铸成钢锭，加热并经锻造开坯，加热温度1100℃，保温4h后进行锻造，控制终锻温度为1000℃，最终锻造成Φ＝92mm的棒料，而后进行风冷，风冷后车削剥皮至Φ＝90mm。
实施例3：按照表1-1和表1-2所示的化学成分电炉冶炼，并进行LF精炼和VD真空处理，而后浇铸成320mm×425mm连铸坯，控制连铸坯首先在预热段加热至600℃，然后在第一加热段继续加热至980℃，保温后继续在第二加热段加热至1200℃，保温8h后进入均热段，均热段温度为1220℃，保温4h后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，控制终轧温度为1000℃，最终轧制成Φ＝100mm的棒料。轧制后空冷，通过超声波探伤和磁粉探伤等检验。
实施例4：按照表1-1和表1-2所示的化学成分电炉冶炼，并进行LF精炼和VD真空处理，而后浇铸成280mm×280mm连铸坯，控制连铸坯首先在预热段加热至620℃，然后在第一加热段继续加热至950℃，保温后继续在第二加热段加热至1150℃，保温6h后进入均热段，均热段温度为1200℃，保温2h后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，控制终轧温度为970℃，最终轧制成Φ＝80mm棒料。轧制后空冷，而后进行砂轮剥皮处理，并经过超声波探伤和磁粉探伤等检验。
实施例5：按照表1-1和表1-2所示的化学成分电炉冶炼，并进行LF精炼和VD真空处理，而后浇铸成320mm×425mm连铸坯，控制连铸坯首先在预热段加热至600℃，然后在第一加热段继续加热至950℃，保温后继续在第二加热段加热至1200℃，保温8h后进入均热段，均热段温度为1230℃，保温后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，轧制成中间坯，控制第一终轧温度为1050℃，中间坯尺寸220mm×220mm，轧后空冷。而后再将中间坯预热段加热至680℃，第一加热段加热至1050℃，第二加热段加热至1200℃，保温6h后进入均热段，均热温度1220℃，出炉经高压水除鳞后开始轧制，控制第二终轧温度为950℃，成品棒材规格为Φ＝60mm。轧制后空冷，而后经过超声波探伤和磁粉探伤等检验。
实施例6：按照表1-1和表1-2所示的化学成分电炉冶炼，并进行精炼和真空处理，而后浇铸成280mm×280mm连铸坯，控制连铸坯首先在预热段加热至680℃，然后在第一加热段继续加热至900℃，保温后继续在第二加热段加热至1180℃，保温6h后进入均热段，均热段温度为1200℃，保温后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，轧制成中间坯，控制第一终轧温度为1000℃，中间坯尺寸140mm×140mm。而后再将中间坯预热至700℃，第一加热段加热至1100℃，第二加热段加热至1220℃，保温5h后进入均热段，均热温度1220℃，出炉经高压水除鳞后开始轧制，控制第二终轧温度为920℃，成品棒材规格为Φ＝30mm。轧制后空冷，而后进行车削剥皮处理，经过超声波探伤和磁粉探伤等检验。
对比例1：实施方式同实施例1，按照表1-1和表1-2所示的化学成分电炉冶炼，并进行精炼和真空处理，而后连铸成280mm×280mm的方坯，控制连铸坯首先在预热段加热至600℃，然后在第一加热段继续加热至980℃，保温后继续在第二加热段加热至1200℃，保温后进入均热段，均热段温度为1220℃，保温后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，控制终轧温度为1000℃，连轧成Φ＝90mm的棒材。轧制后空冷，650℃退火处理，经过超声波探伤和磁粉探伤等检验。
对比例2：实施方式同实施例2，按照表1-1和表1-2所示的化学成分在150kg真空感应炉上进行冶炼。钢水浇铸成钢锭，加热并经锻造开坯，加热温度1100℃，保温4h后进行锻造，控制终锻温度为1000℃，最终锻造成Φ＝92mm棒料，缓冷后车削剥皮至Φ＝90mm。
对比例3：实施方式同实施例4，按照表1-1和表1-2所示的化学成分电炉冶炼，并进行精炼和真空处理，而后连铸成280mm×280mm的方坯，控制连铸坯首先在预热 段加热至680℃，然后在第一加热段继续加热至900℃，保温后继续在第二加热段加热至1180℃，保温后进入均热段，均热段温度为1200℃，保温后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，控制终轧温度为960℃，连轧成Φ＝90mm的棒材。轧制后空冷，650℃退火处理，经过超声波探伤和磁粉探伤等检验。
对比例4：实施方式同实施例5，按照表1-1和表1-2所示的化学成分电炉冶炼，并进行精炼和真空处理，而后浇铸成320mm×425mm的连铸坯，控制连铸坯在预热段加热至600℃，然后在第一加热段继续加热至950℃，保温后继续在第二加热段加热至1200℃，保温后进入均热段，均热段温度为1230℃，保温后进行后续轧制。钢坯出加热炉经高压水除鳞后开始轧制，轧制成中间坯，控制第一终轧温度为1050℃，中间坯尺寸为220mm×220mm。而后将中间坯预热段加热至680℃，第一加热段加热至1050℃，第二加热段加热至1200℃，保温后进入均热段，均热温度1220℃，出炉经高压水除鳞后开始轧制，控制第二终轧温度为950℃，成品棒材规格为Φ＝60mm。轧制后空冷，经过超声波探伤和磁粉探伤等检验。
表1-1列出了实施例1-6的高强韧易切削非调质圆钢和对比例1-4的对比钢的各化学元素的质量百分配比。
表1-1.(wt.％，余量为Fe和除了P、N、O、Ti以及Ca以外的其他不可避免的杂质)
Figure PCTCN2022071570-appb-000001
表1-2列出了由实施例1-6的高强韧易切削非调质圆钢和对比例1-4的对比钢的各化学元素的质量百分含量计算得到的淬透性临界理想直径DI、碳当量Ceq、微合金系数r M/N、贝氏体转变温度T B。
表1-2.
编号 DI值 微合金元素系数r M/N 碳当量Ceq(％) 贝氏体转变温度T B(℃)
实施例1 6.6 4.8 0.76 550
实施例2 7.5 8.4 0.82 539
实施例3 5.4 5.2 0.78 548
实施例4 5.8 3.9 0.74 558
实施例5 6.3 5.5 0.78 563
实施例6 8.8 9.9 0.84 519
对比例1 9.1 6.2 0.83 524
对比例2 4.3 4.1 0.72 566
对比例3 6.7 3.8 0.80 538
对比例4 5.1 3.4 0.85 507
上表中，DI、微合金元素系数r M/N、碳当量Ceq、贝氏体转变温度T B分别按照上文中列出的相关表达式计算。
表2列出了实施例1-6的非调质圆钢和对比例1-4的对比钢在制造方法中采用的具体工艺参数。
表2.
Figure PCTCN2022071570-appb-000002
在表2中，实施例5、实施例6和对比例4这三种实施方式，在轧制过程中，是将钢坯先轧制到各自指定的中间坯尺寸，而后再次进行加热和轧制到最终成品尺寸。
将得到的实施例1-6的非调质圆钢和对比例1-4的对比钢分别取样，并参考GB/T 2975制备试样，按照GB/T 228.1和GB/T 229分别进行拉伸试验和冲击试验，获得各实施例和对比例钢板的力学性能。
对非调质圆钢采用普通车床进行切削加工，搜集切屑来评价钢材的切削性能：切 屑容易破断的颗粒状评价为“好”，而连续不容易破断的螺旋状切屑则评价为“差”，介于两者之间切屑呈“C”型的评价为“中”。将所得各实施例和对比例的力学性能和切削性能的测试试验结果列于表3中。
表3列出了实施例1-6的高强韧易切削非调质圆钢和对比例1-2的对比钢的测试试验结果。
表3.
Figure PCTCN2022071570-appb-000003
注：表3中各栏中的多组数据表示两次或三次的测试结果。
从表3可以看出，本发明所述实施例1-6的高强韧易切削非调质圆钢的综合性能明显优于对比例1-4的对比钢。在本发明中，实施例1-6高强韧易切削非调质圆钢的抗拉强度R m≥1000MPa，延伸率A≥12％，断面收缩率Z≥35％，夏比冲击功A ku≥27J，其不仅具有良好的冲击韧性和塑性，还具有良好的抗疲劳性能，易于切削，可以满足汽车和工程机械等需要高强韧钢材的场合的使用需求。
继续参见表1-1、表1-2、表2和表3，可以看出，对比例1的化学元素成分和相关工艺均符合本发明设计要求，但相较于实施例1-6，对比例1的淬透性临界理想直径DI为9.1，并不在优选的5.0～9.0之间，因此对比例1相对于实施例1-6的非调质圆钢的冲击功较低.
此外，在对比例2-4中，这三个对比例在化学元素成分设计过程中均存在不符合本发明设计规范要求的参数。因此，相较于实施例1-6的非调质圆钢，对比例2和对比例3的对比钢材的强度均比较低，而对比例4的对比钢材的韧性较低，对比例3和对比例4使用效果不佳，对比例3制备的曲轴冲击功低至23J，对比例4制备的曲轴在切削过程中不容易断屑，导致加工效率低，不能满足使用的要求。
图1为实施例2的非调质圆钢在500倍光学显微镜下的微观组织金相照片。
从图1可以看出，实施例2的非调质圆钢微观组织以贝氏体为主，该圆钢截面上贝氏体的面积百分比≥85％。此外，在实施例2中，非调质圆钢的微观组织中还具有残余奥氏体和少量铁素体+珠光体。
图2为实施例2的非调质圆钢制备的曲轴的截面在500倍光学显微镜下的微观组织金相照片。
从图2中可以看出，实施例2的非调质圆钢制备的曲轴微观组织是贝氏体。
本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (12)

  1. 一种高强韧易切削非调质圆钢，其特征在于，以质量百分比计，各化学元素的含量为：
    C：0.36～0.45％、Si：0.20～0.70％、Mn：1.25～1.85％、Cr：0.15～0.55％、Ni：0.10～0.25％、Mo：0.10～0.25％、Al：0.02～0.05％、Nb：0.001～0.040％、V：0.10～0.25％、S：0.02～0.06％；余量为Fe及不可避免的杂质。
  2. 如权利要求1所述的非调质圆钢，其特征在于，还含有Cu，以质量百分比计，Cu的含量为：0＜Cu≤0.25％。
  3. 如权利要求1所述的非调质圆钢，其特征在于，在所述不可避免的杂质中，以质量百分比计，各化学元素的含量满足下述各项中的至少一项：P≤0.015％；N≤0.015％；O≤0.002％；Ti≤0.003％；Ca≤0.005％。
  4. 如权利要求1所述的非调质圆钢，其特征在于：所述非调质圆钢的淬透性临界理想直径DI的值为5.0～9.0；其中，所述淬透性临界理想直径DI按下式计算，
    DI＝0.54*C*(5.10*Mn-1.12)*(0.70*Si+1)*(0.363*Ni+1)*(2.16*Cr+1)*(3.00*Mo+1)*(0.365*Cu+1)*(1.73*V+1)
    上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
  5. 如权利要求1所述的非调质圆钢，其特征在于，所述非调质圆钢的微合金元素系数r M/N的范围为1.1～9.9；其中，所述微合金系数r M/N按下式计算，
    r M/N＝([Al]/2+[Nb]/7+[V]/4)/[N]
    上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
  6. 如权利要求1所述的非调质圆钢，其特征在于，所述非调质圆钢的碳当量Ceq为0.60～1.0％；其中，所述碳当量Ceq按下式计算：
    Ceq＝[C]+[Mn]/6+([Cr]+[Mo]+[V])/5+([Ni]+[Cu])/15
    上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
  7. 如权利要求1所述的非调质圆钢，其特征在于，所述非调质圆钢的微观组织包括贝氏体，在所述非调质圆钢的任一截面上，所述贝氏体的面积占所述截面面积的85％以上。
  8. 如权利要求7所述的非调质圆钢，其特征在于，所述非调质圆钢的贝氏体转变温度T B为515～565℃；其中，所述贝氏体转变温度T B按下式计算：
    T B＝830-270*C-90*Mn-37*Ni-70*Cr-83*Mo
    上式中各化学元素均代入该化学元素的质量百分含量的百分号前面的数值。
  9. 如权利要求7所述的非调质圆钢，其特征在于，所述非调质圆钢的微观组织还包括 残余奥氏体，以及，铁素体或珠光体中的至少一种。
  10. 如权利要求1所述的非调质圆钢，其特征在于，所述非调质圆钢的抗拉强度Rm≥1000MPa，延伸率A≥12％，断面收缩率Z≥35％，夏比冲击功A ku≥27J。
  11. 一种非调质圆钢的制造方法，其特征在于，包括步骤：
    S1：冶炼和浇铸；
    S2：加热；
    S3：锻造或轧制；
    S4：精整；
    所述非调质圆钢的化学组分，以质量百分比计，为：
    C：0.36～0.45％、Si：0.20～0.70％、Mn：1.25～1.85％、Cr：0.15～0.55％、Ni：0.10～0.25％、Mo：0.10～0.25％、Al：0.02～0.05％、Nb：0.001～0.040％、V：0.10～0.25％、S：0.02～0.06％；余量为Fe及不可避免的杂质。
  12. 如权利要求11所述的制造方法，其特征在于，满足下述制备工艺中的至少一项：
    在所述S2中，控制加热温度为1050～1250℃，保温时间为3～24h；
    在所述S3中，控制终轧温度或终锻温度≥800℃，轧后或锻后冷却。
PCT/CN2022/071570 2021-01-12 2022-01-12 一种高强韧易切削非调质圆钢及其制造方法 WO2022152158A1 (zh)

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