WO2016095721A1 - 一种屈服强度900～1000MPa级调质高强钢及制造方法 - Google Patents

一种屈服强度900～1000MPa级调质高强钢及制造方法 Download PDF

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WO2016095721A1
WO2016095721A1 PCT/CN2015/096639 CN2015096639W WO2016095721A1 WO 2016095721 A1 WO2016095721 A1 WO 2016095721A1 CN 2015096639 W CN2015096639 W CN 2015096639W WO 2016095721 A1 WO2016095721 A1 WO 2016095721A1
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mpa
strength
temperature
steel
quenched
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PCT/CN2015/096639
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French (fr)
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杨阿娜
刘刚
王巍
杨晓臻
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宝山钢铁股份有限公司
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Priority to EP15869229.3A priority Critical patent/EP3235924B1/en
Priority to US15/536,601 priority patent/US20170349966A1/en
Priority to JP2017532159A priority patent/JP6502499B2/ja
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a quenched and tempered high-strength steel with a yield strength of 900-1000 MPa and a manufacturing method thereof, the yield strength is 900-1080 MPa, the tensile strength is 950-1200 MPa, the elongation is >10%, and the impact energy at -40 °C is >40 J.
  • the micro-tissue is tempered martensite.
  • Chinese patent CN102560274A introduces a production method for yielding high-strength steel plates of 1000 MPa grade, using reheating quenching + tempering process, and flattening equipment for steel plates. The requirements are extremely high.
  • Chinese patent CN102134680A introduces a production method of high strength steel with a yield strength of 960MPa, using a lower carbon content design and a higher Cr content, C: 0.07% to 0.09%, Cr: 1.05 to 1.15%, the patent does not contain Nb, Ti, V microalloying elements, high Cr content, is not conducive to welding.
  • Chinese patent CN101397640A introduces a production method of yielding 960Mpa grade high strength steel plate, which adopts high Mo content design and high tempering temperature, Mo content is 0.45-0.57%, and tempering temperature is 550-600 °C.
  • composition design in the prior art does not control the comprehensive properties of the joint plastic toughness, nor does it improve the strength and toughness of the finished steel sheet by controlling inclusions and texture properties.
  • the object of the present invention is to provide a quenched and tempered high strength steel with a yield strength of 900 to 1000 MPa. And the manufacturing method thereof, the microstructure of the high-strength steel is tempered martensite, the yield strength is 900-1080 MPa, the tensile strength is 950-1200 MPa, the elongation is >10%, and the impact energy at -40 °C is >40 J.
  • a quenched and tempered high-strength steel with a yield strength of 900 to 1000 MPa the chemical composition weight percentage is: C: 0.16 to 0.20%, Si: 0.10 to 0.30%, Mn: 0.80 to 1.60%, Cr: 0.20 to 0.70%, Mo: 0.10 to 0.45%, Ni: 0.10 to 0.50%, Nb: 0.010 to 0.030%, Ti: 0.010 to 0.030%, V: 0.010 to 0.050%, B: 0.0005 to 0.0030%, Al: 0.02 to 0.06%, Ca: 0.001 ⁇ 0.004%, N: 0.002 to 0.005%, P ⁇ 0.020%, S ⁇ 0.010%, O ⁇ 0.008%, and the rest are Fe and unavoidable impurities.
  • the yield strength of the 900-1000 MPa grade quenched and tempered high-strength steel is 900-1080 MPa
  • the tensile strength is 950-1200 MPa
  • the elongation is >10%
  • the impact energy at -40 °C is >40 J
  • the microstructure is back. Fire martensite.
  • composition design of the present invention is a composition design of the present invention:
  • Carbon solid solution strengthening, adjusting the strength and plastic toughness of martensite structure.
  • Silicon 0.10% or more of Si can play a better deoxidation effect, Si exceeds 0.30%, and it is easy to produce red iron sheet.
  • Si content is high, the toughness of martensitic high-strength steel is easily deteriorated.
  • the silicon content of the present invention ranges from 0.10 to 0.30. %.
  • Mn element content of 0.8% or more can improve the hardenability of steel, and Mn content of more than 1.6% is likely to cause segregation and inclusions such as MnS, and deteriorate the toughness of martensitic high-strength steel.
  • the Mn content of the present invention ranges from 0.80 to 1.60%. .
  • Chromium Cr content above 0.2% can improve the hardenability of steel, which is beneficial to form a full martensite structure during quenching. Cr will form Cr carbides in the range of 400-550 °C tempering temperature, with anti-intermediate temperature. The effect of temper softening, Cr content exceeding 0.70% will cause a large fire when welding The flower affects the quality of the weld, and the Cr content of the present invention ranges from 0.20 to 0.70%.
  • Molybdenum 0.10% or more of Mo element can improve the hardenability of steel, which is beneficial to form a full martensite structure during quenching; Mo will react with C to form compound particles at a high temperature of 400 ° C or higher, and has high temperature temper softening resistance. And the softening effect of the welded joint, if the Mo content is too high, the carbon equivalent is increased, the weldability is deteriorated, and Mo is a precious metal, which increases the cost, and the Mo content of the present invention ranges from 0.10 to 0.45%.
  • Nickel 0.10% or more of Ni element has a fine martensite structure and improves the toughness of steel. If the Ni content is too high, the carbon equivalent is increased, the weldability is deteriorated, and Ni is a precious metal, which increases the cost, and the Ni of the present invention. The content ranges from 0.10 to 0.50%.
  • Niobium, titanium and vanadium are microalloying elements, forming nanoscale precipitates with elements such as C and N, inhibiting the growth of austenite grains during heating; Nb can increase the non-recrystallization critical temperature Tnr , enlarge the production window; fine precipitate particles of Ti can improve the welding performance; V reacts with N and C during the tempering process to precipitate nano-scale V(C,N) particles, which can increase the strength of the steel; It is 0.010 to 0.030%, the titanium content is in the range of 0.010 to 0.030%, and the vanadium content is in the range of 0.010 to 0.050%.
  • B Boron: A small amount of B can improve the hardenability of steel and increase the strength of steel. B exceeding 0.0030% is prone to segregation, forming a boron-boron compound, which seriously deteriorates the toughness of steel.
  • the boron content of the present invention ranges from 0.0005 to 0.0030%.
  • Aluminum is used as a deoxidizer.
  • the addition of 0.02% or more of Al to the steel can refine the grains and improve the impact toughness.
  • the AL content of more than 0.06% is prone to cause oxide inclusion defects of Al.
  • the Al content of the present invention ranges from 0.02 to 0.06. %.
  • Ca More than 0.001% of Ca can act as a purifying agent in the steel smelting process to improve the toughness of the steel; a Ca content exceeding 0.004% tends to form a larger Ca compound, which in turn deteriorates the toughness, and the Ca content of the present invention
  • the range is 0.001 to 0.004%.
  • the present invention requires strict control of the range of N elements, and more than 0.002% of N elements can react with V and C during tempering to form nano-sized V(C,N) particles for precipitation strengthening, during the welding process.
  • the softening zone can also be softened by precipitation strengthening; the N content of more than 0.005% tends to cause coarse precipitate particles to form and deteriorate the toughness.
  • the N content of the present invention ranges from 0.002 to 0.005%.
  • Phosphorus, sulfur and oxygen P, S and O as impurity elements affect the plasticity and toughness of steel, the present invention
  • the control range is P ⁇ 0.020%, S ⁇ 0.010%, and O ⁇ 0.008%.
  • the invention controls 0.8% ⁇ Mo + 0.8Ni + 0.4Cr + 6V ⁇ 1.3%, and is mainly used for ensuring the equal-strength matching welding of 900-1000 MPa high-strength steel, adjusting the strength and low-temperature toughness of the heat affected zone of the welding, and reaching the base metal. The best match between steel strength and low temperature toughness.
  • Mo, Ni and Cr can reduce the critical cooling rate of steel, improve the hardenability of steel and improve the strength of welded joints; Mo reacts with C to form compounds at high temperature, which has the effect of resisting the softening of welded joints; Mo and Ni The elements all have fine structure and improve the toughness; V and N react to form nano-scale V(C,N) particles to resist joint softening; Mo, Ni, Cr and V elements can adjust the welding heat influence according to the strength of the base metal. The strength and toughness of the zone. Less than 0.8% of welded joints have low strength and low temperature toughness; above 1.3% of welded joints have high strength and are prone to weld cracks.
  • the sulfide of the steel species can be spheroidized to improve the low temperature toughness and weldability of the steel.
  • the invention discloses a production method of quenched and tempered high-strength steel with a yield strength of 900-1000 MPa, comprising the following steps:
  • the chemical composition weight percentage is: C: 0.16 to 0.20%, Si: 0.10 to 0.30%, Mn: 0.80 to 1.60%, Cr: 0.20 0.70%, Mo: 0.10 to 0.45%, Ni: 0.10 to 0.50%, Nb: 0.010 to 0.030%, Ti: 0.010 to 0.030%, V: 0.010 to 0.050%, B: 0.0005 to 0.0030%, Al: 0.02 to 0.06 %, Ca: 0.001 to 0.004%, N: 0.002 to 0.005%, P ⁇ 0.020%, S ⁇ 0.010%, O ⁇ 0.008%, and the rest are Fe and unavoidable impurities, and the above elements simultaneously satisfy the following relationship:
  • Ceq 0.51 ⁇ 0.60%, Ceq C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15; 0.8% ⁇ Mo+0.8Ni+0.4Cr+6V ⁇ 1.3%; 3.7 ⁇ Ti / N ⁇ 7.0; 1.0 ⁇ Ca / S ⁇ 3.0;
  • the slab is heated in a furnace at 1150 ⁇ 1270°C, and the heat is started after the core of the slab is heated to the furnace temperature, and the holding time is >1.5h;
  • the single-stand reciprocating rolling or multi-stand hot rolling is used to roll the casting blank to the target thickness, and the rolling reduction rate of the last rolling is >15%; the finishing rolling temperature is 820-920 °C, and the finishing rolling temperature Tf is satisfied.
  • Tnr 887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si;
  • Bs 630-45Mn-40V-35Si-30Cr-25Mo-20Ni;
  • Quenching, quenching heating temperature is Ac 3 + (30 ⁇ 80) ° C, the core of the steel plate to the furnace temperature began to heat, heat 5 ⁇ 40min, to obtain a full martensite structure;
  • the tempering temperature is 400 ⁇ 550 ° C
  • the heart of the steel plate after the furnace temperature is reached the insulation is maintained for 20 ⁇ 180min, and the quenched and tempered high-strength steel with yield strength of 900 ⁇ 1000MPa is obtained.
  • the yield strength of the quenched and tempered high-strength steel with a yield strength of 900-1000 MPa is 900-1080 MPa
  • the tensile strength is 950-1200 MPa
  • the elongation is >10%
  • the impact energy at -40 °C is >40 J
  • the microstructure is tempered. Martensite.
  • the symbol of each element in -16Cu+67Mo and V>e 5.3-2.53C-0.16Si-0.8
  • the control heating temperature is greater than 1150 ° C, the core holding time > 1.5 h can ensure the alloy element is fully solid solution; when the heating temperature exceeds 1270 ° C, the austenite grains grow excessively, causing the intergranular bond weakening Cracks are easily generated during rolling; in addition, the heating temperature exceeding 1270 °C easily causes decarburization on the surface of the slab, which affects the mechanical properties of the finished product.
  • the finish rolling temperature is greater than Ar 3 in order to ensure rolling in the austenite zone.
  • the finish rolling temperature is less than Tnr in order to ensure rolling in the austenite non-recrystallization zone, and rolling in the austenite non-recrystallization zone can be refined.
  • the grain structure and the martensite structure after cooling the grain size and toughness of the steel after the subsequent heat treatment have certain heritability, so the strength and toughness of the steel after heat treatment can be improved.
  • the large deformation amount rolling is performed to form sufficient deformation energy in the non-recrystallization region, and austenite recrystallization is induced in the Ar 3 to Tnr temperature range to refine the crystal grains.
  • the heating temperature is lower than Ac 3 +30 ° C, and the holding time of the steel plate to the furnace temperature is less than 5 min, the alloy is difficult to fully dissolve; and the heating temperature is greater than Ac 3 +80 ° C, the core of the steel plate is to the furnace.
  • the temperature after the temperature is longer than 40 min, the austenite grains are easy to grow.
  • the tempering temperature of the steel of the chemical composition system of the present invention exceeds 400 ° C and the core portion of the steel sheet reaches the furnace temperature for more than 20 minutes, the supersaturated carbon atoms in the quenched martensite are desolvated to form spherical Fe. 3 C cementite, alloys Mo and V react with C at this temperature and form fine alloy carbides, which can improve the ductility and toughness of steel while effectively removing the internal stress of steel.
  • the tempering temperature exceeds 550 ° C or the high holding time is too long, the spherical Fe 3 C cementite and alloy carbide will coarsen, which will deteriorate the toughness of the steel and reduce the strength of the steel; by adjusting the tempering temperature and tempering time, Ensure the best match between strength and toughness.
  • the invention adopts controlled rolling and controlled cooling and off-line quenching + tempering process, and is controlled from the aspects of chemical composition design, base metal structure, quenching heating temperature and tempering heating temperature to ensure the elongation of steel while achieving ultra high strength. Good performance such as low temperature impact toughness.
  • the present invention controls the strength and toughness of the base metal welded joint by controlling the content and matching of elements such as Mo, Ni, Cr, V, etc., and improves the base metal steel plate and welding by controlling the Ti, N ratio, Ca, S ratio.
  • the toughness of the joint using the genetic properties of the tissue properties to improve the toughness of the finished steel sheet through the process.
  • FIG. 1 is a view showing a typical metallographic structure of a test steel according to a first embodiment of the present invention.
  • Example 2 is a view showing a typical metallographic structure of a test steel according to Example 3 of the present invention.
  • Fig. 3 is a view showing a typical metallographic structure of a test steel according to Example 6 of the present invention.
  • the production process of the ultra-high strength steel of the invention is: converter or electric furnace steelmaking ⁇ furnace refining ⁇ continuous casting ⁇ heating ⁇ rolling ⁇ cooling ⁇ heat treatment.
  • the method for manufacturing 900-1000 MPa grade quenched and tempered high-strength steel according to Embodiments 1 to 10 of the present invention comprises the following steps:
  • Smelting and casting smelting is carried out using a 50 kg vacuum electric furnace. The composition is as shown in Table 1. The smelted molten steel is cast into a 120 mm thick slab and placed in an electric furnace for heating.
  • Cooling For the rolled product after rolling, laminar cooling is performed on-line, and the final cooling temperature control range is 480 to Bs ° C, and Bs is the bainite transformation starting temperature; coiling, air cooling to room temperature.
  • quenching heat treatment process quenching heat treatment process, quenching heating temperature is austenite transformation end temperature Ac 3 + (30 ⁇ 80) ° C, quenching heating time is 5 to 40 min after the heart of the steel plate to the furnace temperature; quenching cooling speed V> e (5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B) °C / s; quenching to (Ms-150) ° C or less;
  • tempering heat treatment process the tempering temperature is 400-550 ° C, and the tempering time is 20-180 min after the core of the steel plate reaches the furnace temperature, and the 900-1000 MPa grade quenched and tempered high-strength steel of the invention is obtained.
  • Figures 1 to 3 show photographs of the metallographic structure of the test steels of Examples 1, 3 and 6. From the metallographic photographs of Figures 1 to 3, it can be seen that the metallographic structure of the finished steel sheet is a uniform equiaxed back. Martensite, and finely organized.
  • the invention adopts controlled rolling and controlled cooling and off-line quenching + tempering process, and is controlled from the aspects of chemical composition design, base metal structure, quenching heating temperature and tempering heating temperature to ensure the elongation of steel while achieving ultra high strength. Good performance such as low temperature impact toughness.

Abstract

一种屈服强度900～1000MPa级调质高强钢及其生产方法，其化学成分重量百分比为：C 0.16～0.20％，Si 0.10～0.30％，Mn 0.80～1.60％，Cr 0.20～0.70％，Mo 0.10～0.45％，Ni 0.10～0.50％，Nb 0.010～0.030％，Ti 0.010～0.030％，V 0.010～0.050％，B 0.0005～0.0030％，Al 0.02～0.06％，Ca 0.001～0.004％，N 0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免杂质，且：Ceq 0.51～0.60％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％。该高强钢采用控轧控冷和离线淬火+回火工艺，生产出的钢板屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J。

Description

一种屈服强度900～1000MPa级调质高强钢及制造方法 技术领域
本发明涉及一种屈服强度900～1000MPa级调质高强钢及制造方法，其屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J，显微组织为回火马氏体。
背景技术
采用高强度易焊接结构钢制造工程机械的梁结构、起重机的吊臂和自卸车的车体等移动设备的构件，都会减轻设备自重，减少燃料消耗，提高工作效率。随着国际竞争的加剧，采用高强度易焊接结构钢制造港口机械、矿山机械、挖掘机、装载机的梁结构、起重机的吊臂和自卸车的车体等移动设备的构件已经成为趋势。由于工程机械高性能、大型化、轻量化的发展要求，工程机械用钢的强度级别不断攀升，从500～600MPa级快速上升到700MPa、900MPa、1000MPa乃至1100MPa。工程机械用超高强钢由于其苛刻的使用环境和受力条件，对钢材质量有严格的要求，包括强度性能、冲击性能、折弯性能、焊接性能和板形等。
目前国内生产屈服900～1000MPa级别的高强度钢板的企业很少，中国专利CN102560274A介绍了一种屈服1000MPa级别高强度厚钢板的生产方法，采用的是再加热淬火+回火工艺，对钢板开平设备要求极高。中国专利CN102134680A介绍了一种屈服强度960MPa级高强钢的生产方法，采用较低的碳含量设计和较高的Cr含量，C：0.07％～0.09％，Cr：1.05～1.15％，该专利不含Nb、Ti、V微合金元素，Cr含量较高，不利于焊接。中国专利CN101397640A介绍了一种屈服960Mpa级别高强钢板的生产方法，采用较高的Mo含量设计和较高的回火温度，Mo含量0.45～0.57％，回火温度550～600℃。
现有技术中的成分设计没有控制接头塑韧性综合性能，也没有通过控制夹杂物及组织性能遗传性改善成品钢板的强度和韧性。
发明内容
本发明的目的在于提供一种屈服强度900～1000MPa级调质高强度钢 及其制造方法，该高强度钢的显微组织为回火马氏体，屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J。
为了达到上述目的，本发明提供的技术方案是：
一种屈服强度900～1000MPa级调质高强钢，其化学成分重量百分比为：C：0.16～0.20％，Si：0.10～0.30％，Mn：0.80～1.60％，Cr：0.20～0.70％，Mo：0.10～0.45％，Ni：0.10～0.50％，Nb：0.010～0.030％，Ti：0.010～0.030％，V：0.010～0.050％，B：0.0005～0.0030％，Al：0.02～0.06％，Ca：0.001～0.004％，N：0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免的杂质，上述元素同时需满足如下关系式：Ceq 0.51～0.60％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％。
进一步，所述的屈服强度900～1000MPa级调质高强钢的屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J，显微组织为回火马氏体。
在本发明的成分设计中：
碳：固溶强化，调整马氏体组织的强度和塑韧性，经试验，再加热淬火后低碳马氏体的抗拉强度与C含量的关系呈如下关系：Rm＝2510C(％)+790(MPa)，Rm为抗拉强度，C含量在0.16％以上才可以保证淬火态抗拉强度大于1100MPa，再通过回火进一步降低强度，改善韧性；C含量较高会导致整体C当量的提高，焊接时容易产生裂纹，本发明的C含量范围为0.16～0.20％。
硅：0.10％以上的Si可以起到较好的脱氧作用，Si超过0.30％容易产生红铁皮，Si含量较高时容易恶化马氏体高强钢的韧性，本发明的硅含量范围为0.10～0.30％。
锰：Mn元素在0.8％以上可以提高钢的淬透性，Mn含量超过1.6％容易产生偏析和MnS等夹杂物，恶化马氏体高强钢的韧性，本发明的Mn含量范围为0.80～1.60％。
铬：Cr元素在0.2％以上可以提高钢的淬透性，有利于在淬火时形成全马氏体组织，Cr在400～550℃回火温度左右范围内会形成Cr的碳化物，具有抗中温回火软化的作用，Cr含量超过0.70％在焊接时会出现较大的火 花，影响焊接质量，本发明的Cr含量范围为0.20～0.70％。
钼：0.10％以上的Mo元素可以提高钢的淬透性，有利于在淬火时形成全马氏体组织；Mo在400℃以上的高温下会与C反应形成化合物颗粒，具有抗高温回火软化和焊接接头软化的作用，Mo含量太高会导致碳当量提高，恶化焊接性能，同时Mo属于贵金属，会提高成本，本发明的Mo含量范围为0.10～0.45％。
镍：0.10％以上的Ni元素具有细化马氏体组织，改善钢的韧性的作用，Ni含量太高会导致碳当量提高，恶化焊接性能，同时Ni属于贵金属，会提高成本，本发明的Ni含量范围为0.10～0.50％。
铌、钛和钒：Nb、Ti和V为微合金元素，与C、N等元素形成纳米级析出物，在加热时抑制奥氏体晶粒的长大；Nb可以提高未再结晶临界温度Tnr，扩大生产窗口；Ti的细小析出物颗粒可以改善焊接性能；V在回火过程中与N和C反应析出纳米级V(C,N)颗粒，可以提高钢的强度；本发明的铌含量范围为0.010～0.030％，钛含量范围为0.010～0.030％，钒含量范围为0.010～0.050％。
硼：微量的B可以提高钢的淬透性，提高钢的强度，超过0.0030％的B容易产生偏析，形成碳硼化合物，严重恶化钢的韧性，本发明的硼含量范围为0.0005～0.0030％。
铝：Al用作脱氧剂，钢中加入0.02％以上的Al可细化晶粒，提高冲击韧性，AL含量超过0.06％容易产生Al的氧化物夹杂缺陷，本发明的Al含量范围为0.02～0.06％。
钙：超过0.001％的Ca元素可以在钢冶炼过程中的起到净化剂作用，改善钢的韧性；Ca含量超过0.004％容易形成尺寸较大的Ca的化合物，反而会恶化韧性，本发明Ca含量范围为0.001～0.004％。
氮：本发明要求严格控制N元素的范围，0.002％以上的N元素在回火过程中可以与V和C反应形成纳米级的V(C，N)粒子起到析出强化的作用，在焊接过程中也可以通过析出强化抵抗热影响区软化；N含量超过0.005％容易导致形成粗大的析出物颗粒，恶化韧性。本发明N含量范围为0.002～0.005％。
磷、硫和氧：P、S和O作为杂质元素影响钢的塑、韧性，本发明对 其控制范围分别为P≤0.020％，S≤0.010％，O≤0.008％。
对于离线淬火+回火型屈服900～1000MPa高强钢，碳当量Ceq需满足：Ceq 0.51～0.60％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/150，Ceq太低容易出现焊接接头软化，Ceq太高容易出现焊接微裂纹。
本发明通过控制0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％，主要用于保证900～1000MPa高强钢的等强匹配焊接，调节焊接热影响区的强度和低温韧性，达到与母材钢板强度和低温韧性的最佳匹配。其中Mo、Ni和Cr元素都可以降低钢的临界冷却速度，提高钢的淬透性，提高焊接接头的强度；Mo在高温下与C反应形成化合物，具有抵抗焊接接头软化的作用；Mo和Ni元素都具有细化组织，改善韧性的作用；V与N反应生成纳米级V(C，N)颗粒可以抵抗接头软化；Mo、Ni、Cr和V元素的搭配可以根据母材强度调节焊接热影响区的强度和韧性。低于0.8％焊接接头的强度和低温韧性都较低；高于1.3％焊接接头强度偏高，容易产生焊接裂纹。
通过控制3.7≤Ti/N≤7.0可以保护钢中的B原子，使得B充分固溶，提高淬透性，合适的Ti、N比有利于控制Ti析出物颗粒的尺寸改善母材和接头的强度和韧性。
通过控制1.0≤Ca/S≤3.0可以使钢种的硫化物球化，改善钢的低温韧性和焊接性能。
本发明的一种屈服强度900～1000MPa级调质高强钢的生产方法，包括如下步骤：
1)铁水冶炼、铸造
按下述化学成分采用转炉或电炉炼钢、精炼，铸造形成铸坯；化学成分重量百分比为：C：0.16～0.20％，Si：0.10～0.30％，Mn：0.80～1.60％，Cr：0.20～0.70％，Mo：0.10～0.45％，Ni：0.10～0.50％，Nb：0.010～0.030％，Ti：0.010～0.030％，V：0.010～0.050％，B：0.0005～0.0030％，Al：0.02～0.06％，Ca：0.001～0.004％，N：0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免的杂质，上述元素同时需满足如下关系式：
Ceq 0.51～0.60％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
2)加热
将铸坯于1150～1270℃的炉中加热，待铸坯心部到炉温后开始保温，保温时间>1.5h；
3)轧制
采用单机架往复轧制或多机架热连轧将铸坯轧至目标厚度，轧制最后一道次轧制压下率>15％；终轧温度为820～920℃，同时终轧温度Tf满足：Ar3<Tf<Tnr；其中，Ar3为亚共析钢奥氏体向铁素体转变开始温度，Ar3＝901-325C-92Mn-126Cr-67Ni-149Mo；Tnr为未再结晶临界温度：
Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si；
4)冷却
将热轧后的轧件在480～Bs℃温度范围内卷取，然后空冷至室温；
其中，Bs＝630-45Mn-40V-35Si-30Cr-25Mo-20Ni；
5)热处理
淬火，淬火加热温度为Ac3+(30～80)℃，钢板心部到炉温后开始保温，保温5～40min，得到全马氏体组织；其中，Ac3为奥氏体转变结束温度，Ac3＝955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo；淬火冷却速度V>e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s；
回火，回火温度为400～550℃，钢板心部达到炉温后开始保温，保温20～180min，得到屈服强度900～1000MPa级调质高强钢。
进一步，得到的屈服强度900～1000MPa级调质高强钢的屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J，显微组织为回火马氏体。
本发明涉及的如下关系式：Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15，Mo+0.8Ni+0.4Cr+6V，Ti/N，Ca/S中各元素符号表示对应元素的重量百分含量；涉及的如下计算公式：Ar3＝901-325C-92Mn-126Cr-67Ni-149Mo，Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si，Bs＝630-45Mn-40V-35Si-30Cr-25Mo-20Ni，Ac3＝955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo以及V>e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)中各元素符号表示对应元素的重量百分含量×100。
在本发明的屈服强度900～1000MPa级调质高强钢的生产方法中：
在铸坯加热工艺中，控制加热温度大于1150℃、心部保温时间>1.5h可以保证合金元素充分固溶；加热温度超过1270℃时奥氏体晶粒过度长大，引起晶间结合力减弱，在轧制时容易产生裂纹；另外加热温度超过1270℃容易引起钢坯表面脱碳，对成品力学性能造成影响。
终轧温度大于Ar3是为了保证在奥氏体区轧制，终轧温度小于Tnr是为了保证在奥氏体未再结晶区轧制，在奥氏体未再结晶区轧制可以细化奥氏体晶粒和冷却后马氏体组织，经后续热处理后钢的晶粒度和韧性具有一定遗传性，因此可以改善热处理后钢的强度和韧性。同时，在轧制过程中，进行大变形量轧制是为了在未再结晶区形成足够的变形能，在Ar3～Tnr温度范围内诱发奥氏体再结晶，细化晶粒。
冷却工艺中，在480～Bs℃温度范围内卷取是为了得到细小的贝氏体组织，改善钢的韧性。经后续热处理后，钢的晶粒度和韧性具有一定遗传性，因此可以改善热处理后钢的强度和韧性。
淬火热处理工艺中，加热温度低于Ac3+30℃、钢板心部到炉温后保温时间低于5min时，合金难以充分固溶；而加热温度大于Ac3+80℃、钢板心部到炉温后保温时间大于40min时，奥氏体晶粒容易长大，通过控制淬火加热温度和淬火加热时间在一定窄的范围内，可以保证得到细小的奥氏体晶粒，从而细化淬火后的马氏体组织，改善钢的强韧性。
在回火热处理工艺中，本发明的化学成分体系的钢，回火温度超过400℃并且钢板心部到炉温后保持20min以上时，淬火马氏体中的过饱和碳原子脱溶形成球状Fe3C渗碳体，合金Mo和V在该温度下会与C反应并形成细小的合金碳化物，可以改善钢的塑性和韧性，同时有效去除钢的内应力。回火温度超过550℃或高保温时间过长球状Fe3C渗碳体和合金碳化物发生粗化，反而会恶化钢的韧性，并降低钢的强度；通过调整回火温度和回火时间可以保证强、韧性实现最佳匹配。
本发明的有益效果：
本发明采用控轧控冷和离线淬火+回火工艺，从化学成分设计、母材组织、淬火加热温度、回火加热温度等角度进行控制，保证在实现超高强度的同时，钢的延伸率、低温冲击韧性等性能良好。
与现有技术相比，本发明通过控制Mo、Ni、Cr、V等元素的含量和匹配控制母材焊接接头的强韧性，通过控制Ti、N比，Ca、S比改善母材钢板和焊接接头的韧性，利用组织性能遗传特性通过工艺改善成品钢板的强韧性。
附图说明
图1为本发明实施例1的试验钢典型金相组织图。
图2为本发明实施例3的试验钢典型金相组织图。
图3为本发明实施例6的试验钢典型金相组织图。
具体实施方式
下面结合实施例对本发明做进一步说明。
本发明的超高强钢的生产工艺流程为：转炉或电炉炼钢→炉外精炼→连铸→加热→轧制→冷却→热处理。
本发明实施例1～10的900～1000MPa级调质高强钢的制造方法，包括如下步骤：
1)冶炼、铸造：采用50kg真空电炉进行冶炼，成分如表1所示，将冶炼的钢水浇注成120mm厚的铸坯，放入电炉中加热。
2)轧制：采用多道次将铸坯轧制成目标厚度10mm的钢板，终轧温度为820～920℃，同时终轧温度Tf满足：Ar3<Tf<Tnr；末道次压下率设定17％。
3)冷却：对轧制后的轧件，在线进行层流冷却，终冷温度控制范围为480～Bs℃，Bs为贝氏体转变开始温度；卷取，空冷至室温。
4)淬火热处理工艺：淬火热处理工艺，淬火加热温度为奥氏体转变结束温度Ac3+(30～80)℃，淬火加热时间为钢板心部到炉温后5～40min；淬火冷却速度V>e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s；淬火冷却至(Ms-150)℃以下；
5)回火热处理工艺：回火温度为400～550℃，回火时间为钢板心部到炉温后20～180min，得到本发明的900～1000MPa级调质高强钢。
6)将调质处理后的钢板进行纵向拉伸和纵向冲击试验。
具体成分、工艺参数如表1、表2所示。各实施例样板对应的性能如表3所示。
图1-图3给出了实施例1、3、6试验钢的金相组织照片，从图1-图3金相照片上可以看出，成品钢板的金相组织为均一的等轴状回火马氏体，且组织细密。
本发明采用控轧控冷和离线淬火+回火工艺，从化学成分设计、母材组织、淬火加热温度、回火加热温度等角度进行控制，保证在实现超高强度的同时，钢的延伸率、低温冲击韧性等性能良好。
表1    单位
Figure PCTCN2015096639-appb-000001
表2
Figure PCTCN2015096639-appb-000002
表3
Figure PCTCN2015096639-appb-000003
注：-40℃冲击功试验结果中三列分别代表三个平行试样的测试结果。

Claims (6)

  1. 一种屈服强度900～1000MPa级调质高强钢，其化学成分重量百分比为：C：0.16～0.20％，Si：0.10～0.30％，Mn：0.80～1.60％，Cr：0.20～0.70％，Mo：0.10～0.45％，Ni：0.10～0.50％，Nb：0.010～0.030％，Ti：0.010～0.030％，V：0.010～0.050％，B：0.0005～0.0030％，Al：0.02～0.06％，Ca：0.001～0.004％，N：0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免的杂质，上述元素同时需满足如下关系式：
    Ceq 0.51～0.60％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；
    0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0。
  2. 根据权利要求1所述的屈服强度900～1000MPa级调质高强钢，其特征在于，其显微组织为回火马氏体。
  3. 根据权利要求1所述的屈服强度900～1000MPa级调质高强钢，其特征在于，其屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J。
  4. 一种屈服强度900～1000MPa级调质高强钢的生产方法，其特征在于，包括如下步骤：
    1)冶炼、铸造
    按下述化学成分采用转炉或电炉炼钢、精炼，铸造形成铸坯；化学成分重量百分比为：C：0.16～0.20％，Si：0.10～0.30％，Mn：0.80～1.60％，Cr：0.20～0.70％，Mo：0.10～0.45％，Ni：0.10～0.50％，Nb：0.010～0.030％，Ti：0.010～0.030％，V：0.010～0.050％，B：0.0005～0.0030％，Al：0.02～0.06％，Ca：0.001～0.004％，N：0.002～0.005％，P≤0.020％，S≤0.010％，O≤0.008％，其余为Fe及不可避免的杂质，上述元素同时需满足如下关系式：
    Ceq 0.51～0.60％，Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15；0.8％≤Mo+0.8Ni+0.4Cr+6V≤1.3％；3.7≤Ti/N≤7.0；1.0≤Ca/S≤3.0；
    2)加热
    将铸坯于1150～1270℃的炉中加热，待铸坯心部到炉温后开始保温，保温时间>1.5h；
    3)轧制
    采用单机架往复轧制或多机架热连轧将铸坯轧至目标厚度，轧制最后一道次压下率>15％；终轧温度为820～920℃，同时终轧温度Tf满足：Ar3<Tf<Tnr；其中，Ar3为亚共析钢奥氏体向铁素体转变开始温度，Tnr为未再结晶临界温度：
    Ar3＝901-325C-92Mn-126Cr-67Ni-149Mo；
    Tnr＝887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si；
    4)冷却
    将热轧后的轧件在480～Bs℃温度范围内卷取，然后空冷至室温；
    其中，Bs＝630-45Mn-40V-35Si-30Cr-25Mo-20Ni；
    5)热处理
    淬火，淬火加热温度为Ac3+(30～80)℃，Ac3为奥氏体转变结束温度；
    Ac3＝955-350C-25Mn+51Si+106Nb+100Ti+68Al-11Cr-33Ni-16Cu+67Mo；钢板心部达到炉温后开始保温，保温5～40min；淬火至(Ms-150)℃以下，得到全马氏体组织；其中，Ms为马氏体转变开始温度，
    Ms＝539-423C-30.4Mn-17.7Ni-12.1Cr-11.0Si-7.0Mo；淬火冷却速度V>e(5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B)℃/s；
    回火，回火温度为400～550℃，钢板心部达到炉温后开始保温，保温20～180min，得到屈服强度900～1000MPa级调质高强钢。
  5. 根据权利要求4所述的屈服强度900～1000MPa级调质高强钢的生产方法，其特征在于，该生产方法获得的高强钢板其显微组织为回火马氏体。
  6. 根据权利要求4所述的屈服强度900～1000MPa级调质高强钢的生产方法，其特征在于，该生产方法获得的高强钢板的屈服强度为900～1080MPa，抗拉强度为950～1200MPa，延伸率>10％，-40℃冲击功>40J。
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