CN102418047A - Non-quenched and tempered fatigue-resistant steel plate and manufacturing method thereof - Google Patents
Non-quenched and tempered fatigue-resistant steel plate and manufacturing method thereof Download PDFInfo
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Abstract
Description
技术领域 technical field
本发明属于热轧高强钢生产技术领域，涉及一种抗拉强度达到800MPa级别的非调质处理高耐疲劳性能的钢板及其制造方法。The invention belongs to the technical field of hot-rolled high-strength steel production, and relates to a steel plate with non-quenching and tempering treatment and high fatigue resistance with a tensile strength reaching 800 MPa and a manufacturing method thereof.
背景技术 Background technique
目前工程机械用钢和汽车结构钢中，高强钢的使用量占据一定比例，主要用于制造吊车悬臂，汽车大梁钢等关键部位。由于关系到整体结构的稳定性和使用寿命，所以对高强钢的使用要求和条件非常苛刻。对于这种高强钢的使用要求主要是钢的疲劳性能，从而对制造材料提出的要求是在具备高强度的同时，又具有优良的耐疲劳性能。At present, high-strength steel accounts for a certain proportion of construction machinery steel and automobile structural steel, mainly used in the manufacture of key parts such as crane cantilever and automobile beam steel. Since it is related to the stability and service life of the overall structure, the requirements and conditions for the use of high-strength steel are very strict. The requirement for the use of this high-strength steel is mainly the fatigue performance of the steel, so the requirement for the manufacturing material is to have high strength and excellent fatigue resistance at the same time.
对此，本领域技术人员通常采用不同微合金化的方法制造高强度高耐疲劳性能钢板的工艺技术。In this regard, those skilled in the art usually use different microalloying methods to manufacture high-strength and high-fatigue-resistant steel plates.
公开号CN101139685A的发明专利申请涉及一种高强度耐疲劳钢材及其制造方法，属特种钢及其冶炼技术领域。该专利申请通过添加适量的Nb、Ti元素进行微合金化，采用复吹转炉冶炼、LF精炼、板坯连铸、高压水除鳞、热轧层流冷却，卷取工艺，生产出成分按重量百分比(wt％)计包括0.07％～0.13％的C、0.15％～0.35％的Si、1.0％～1.3％的Mn、P≤0.025％、S≤0.01％、0.015％～0.020％的Nb、0.01％～0.025％的Ti和0.015％～0.050％的Alt，其余为Fe和微量杂质的高强度耐疲劳钢，这种钢的疲劳极限在应力比R＝0.76时达到510MPa，适用于制造重卡、轻卡等载重车车架的纵梁、横梁等构件。因此，该发明中钢的疲劳强度适合制造低牌号的汽车结构件。The invention patent application with publication number CN101139685A relates to a high-strength fatigue-resistant steel and its manufacturing method, which belongs to the technical field of special steel and its smelting. The patent application is micro-alloyed by adding an appropriate amount of Nb and Ti elements, and adopts double-blow converter smelting, LF refining, slab continuous casting, high-pressure water descaling, hot rolling laminar cooling, and coiling process to produce components by weight. Percentage (wt%) includes 0.07% to 0.13% of C, 0.15% to 0.35% of Si, 1.0% to 1.3% of Mn, P≤0.025%, S≤0.01%, 0.015% to 0.020% of Nb, 0.01% %～0.025% Ti and 0.015%～0.050% Alt, the rest is Fe and trace impurities high-strength fatigue-resistant steel, the fatigue limit of this steel reaches 510MPa when the stress ratio R=0.76, suitable for manufacturing heavy trucks and light trucks Longitudinal beams, beams and other components of truck frames. Therefore, the fatigue strength of the steel in this invention is suitable for manufacturing low-grade automotive structural parts.
公开号CN1957100A的发明专利申请公开了一种耐疲劳裂纹扩展性优异的钢板及其制造方法，属于低合金化钢制造领域。该专利申请提供了一种耐疲劳破坏性能优异的钢板及其制造方法，其提高了针对在各种焊接结构物等的焊接部等内在的裂纹因受到反复应力而扩展的阻抗性。该钢板以质量％计含有：C：0.01％～0.10％、Si：0.03％～0.6％、Mn：0.3％～2％、sol.Al：0.001％～0.1％、N：0.0005％～0.008％，并且根据需要添加一定含量的Nb、Ti、Mo、V、Cr、Cu、Ni、B等合金元素，余量为Fe和杂质，且金相组织以面积率计为30％以上的贝氏体组织，合计5％以下的马氏体组织和珠光体组织，余量是铁素体组织。该发明采用相变强化的成分设计思路，但是最高抗拉强度在700Mpa以下。The invention patent application with the publication number CN1957100A discloses a steel plate with excellent resistance to fatigue crack growth and its manufacturing method, which belongs to the field of low-alloyed steel manufacturing. This patent application provides a steel plate with excellent fatigue fracture resistance and a manufacturing method thereof, which have improved resistance against the propagation of internal cracks in welded parts of various welded structures and the like due to repeated stress. The steel sheet contains, by mass %: C: 0.01% to 0.10%, Si: 0.03% to 0.6%, Mn: 0.3% to 2%, sol.Al: 0.001% to 0.1%, N: 0.0005% to 0.008%, And add a certain amount of alloying elements such as Nb, Ti, Mo, V, Cr, Cu, Ni, B as required, the balance is Fe and impurities, and the metallographic structure is a bainite structure with an area ratio of more than 30%. , a total of less than 5% of the martensite structure and pearlite structure, and the balance is a ferrite structure. This invention adopts the idea of phase transformation strengthening composition design, but the highest tensile strength is below 700Mpa.
目前，不同企业生产的耐疲劳性能的钢的强度一般较低。随着社会和经济的发展，钢铁工业所面临的低碳经济发展，以节省资源、节约能源、保护环境为主要目标，同时轻量化技术也要求不断改善材料的性能，这也是目前钢铁材料发展的趋势。At present, the strength of steel with fatigue resistance produced by different enterprises is generally low. With the development of society and economy, the development of low-carbon economy faced by the iron and steel industry aims to save resources, save energy, and protect the environment. At the same time, lightweight technology also requires continuous improvement of the performance of materials. trend.
发明内容 Contents of the invention
为了解决现有技术中存在的上述问题，本发明提供了一种高强度非调质处理的热轧钢板，所述钢板在具备高强度的同时，也具有良好的耐疲劳性能，能够满足不同行业的需要。In order to solve the above-mentioned problems in the prior art, the present invention provides a high-strength non-tempered hot-rolled steel plate. The steel plate not only has high strength, but also has good fatigue resistance, and can meet the needs of different industries. needs.
本发明提供了一种非调质处理耐疲劳的钢板，所述钢板的化学成分按重量百分计由以下物质组成：C：0.05％～0.15％、Si≤0.1％、Mn：2.0％～3.0％、P≤0.010％、S≤0.002％、Cr：0.2％～1.0％、V：0.02％～0.1％、Ti：0.08％～0.18％、Nb：0.02％～0.06％、N≤0.004％和O≤0.002％，其余为铁Fe和不可避免的杂质，其中，所述钢板的抗拉强度在800MPa以上。The invention provides a non-tempered fatigue-resistant steel plate. The chemical composition of the steel plate is composed of the following substances by weight percentage: C: 0.05% to 0.15%, Si≤0.1%, Mn: 2.0% to 3.0% %, P≤0.010%, S≤0.002%, Cr: 0.2%～1.0%, V: 0.02%～0.1%, Ti: 0.08%～0.18%, Nb: 0.02%～0.06%, N≤0.004% and O ≤0.002%, the rest is iron Fe and unavoidable impurities, wherein, the tensile strength of the steel plate is above 800MPa.
根据本发明的一方面，所述钢板的金相组织为超细多边形铁素体和少量贝氏体，其中多边形铁素体的体积百分比为整个金相组织的85％以上。According to one aspect of the present invention, the metallographic structure of the steel plate is ultra-fine polygonal ferrite and a small amount of bainite, wherein the volume percentage of polygonal ferrite is more than 85% of the entire metallographic structure.
根据本发明的一方面，所述钢板的化学成分按重量百分计可以由以下物质组成：C：0.05％～0.12％、Si≤0.1％、Mn：2.0％～2.6％、P≤0.010％、S≤0.002％、Cr：0.3％～0.8％、V：0.04％～0.08％、Ti：0.10％～0.15％、Nb：0.03％～0.06％、N≤0.004％和O≤0.002％，其余为铁Fe和不可避免的杂质。According to one aspect of the present invention, the chemical composition of the steel plate may be composed of the following substances by weight percentage: C: 0.05%-0.12%, Si≤0.1%, Mn: 2.0%-2.6%, P≤0.010%, S≤0.002%, Cr: 0.3%～0.8%, V: 0.04%～0.08%, Ti: 0.10%～0.15%, Nb: 0.03%～0.06%, N≤0.004% and O≤0.002%, the rest is iron Fe and unavoidable impurities.
本发明还提供了一种制造上述非调质处理耐疲劳的钢板的方法，所述方法包括冶炼工艺、轧制成型工艺及冷却工艺和卷取工艺，其中，在轧制成型工艺中，控制连铸坯的加热温度为1150℃～1250℃，加热时间达100分钟～160分钟；然后，进行控制轧制，粗轧开轧温度为1120℃～1180℃，粗轧终轧温度为1020℃～1060℃，精轧终轧温度控制在850℃～900℃，精轧过程每道次的压下量控制在15％～40％，精轧机架间采用水冷。The present invention also provides a method for manufacturing the above non-tempered fatigue-resistant steel plate, the method includes a smelting process, a rolling forming process, a cooling process and a coiling process, wherein, in the rolling forming process, the control continuous The heating temperature of the slab is 1150°C-1250°C, and the heating time is 100-160 minutes; then, the controlled rolling is carried out, the rough rolling start temperature is 1120°C-1180°C, the rough rolling finish rolling temperature is 1020°C-1060 ℃, the finish rolling temperature is controlled at 850 ℃ ~ 900 ℃, the reduction of each pass in the finish rolling process is controlled at 15% ~ 40%, and water cooling is used between the finish rolling stands.
根据本发明的另一方面，在冶炼工艺中，采用预脱硫工艺，将铁水中的S含量控制在0.005％以下；转炉石灰采用优质石灰，以降低S的掺杂；转炉挡渣全部挡住；将精炼后钢水中的Si和Al含量控制在0.1％和以0.05％下；采用添加钛铁和钛线复合添加的方式来控制铁水中的Ti含量。According to another aspect of the present invention, in the smelting process, a pre-desulfurization process is adopted to control the S content in the molten iron below 0.005%; the converter lime adopts high-quality lime to reduce the doping of S; the converter slag is completely blocked; The content of Si and Al in the molten steel after refining is controlled at 0.1% and 0.05%; the Ti content in the molten iron is controlled by adding ferro-titanium and titanium wire.
根据本发明的另一方面，在冷却工艺和卷取工艺中，将轧制后的坯料进行层流冷却然后进行卷取，冷却速度为5℃/s～20℃/s，卷取温度为500℃～600℃。According to another aspect of the present invention, in the cooling process and the coiling process, the rolled billet is subjected to laminar cooling and then coiled, the cooling rate is 5°C/s-20°C/s, and the coiling temperature is 500 ℃～600℃.
根据本发明的另一方面，粗轧过程可以进行3～5道次轧制，精轧过程可以进行4～6道次轧制。According to another aspect of the present invention, the rough rolling process can be rolled for 3-5 passes, and the finish rolling process can be rolled for 4-6 passes.
根据本发明，在提高钢板的强度的同时，能够使钢板具备良好的耐疲劳性能，从而根据本发明的钢板能够满足工程机械和汽车结构钢用户的使用的要求。According to the present invention, while improving the strength of the steel plate, the steel plate can be provided with good fatigue resistance, so that the steel plate according to the present invention can meet the requirements of users of engineering machinery and automobile structural steel.
具体实施方式 Detailed ways
为了节省资源，使得生产的钢板不仅抗拉强度在800MPa以上，并且具有优良的耐疲劳性能，同时成形性能良好，本发明提供了一种能够降低成本的非调质处理耐疲劳钢板的制造方法，而且在普通热连轧机上就能够实现。In order to save resources, the steel plate produced not only has a tensile strength above 800 MPa, but also has excellent fatigue resistance and good formability. The present invention provides a method for manufacturing a non-tempered fatigue-resistant steel plate that can reduce costs. And it can be realized on a common hot rolling mill.
本发明提供了一种低成本且抗拉强度在800MPa级非调质处理的高强耐疲劳钢及其制造方法。具体地讲，本发明是在碳锰结构钢成分的基础上，通过添加适量的Nb、V、Ti、Cr等微合金元素和采用控轧控冷技术，考虑到普通热连轧机的生产特点，利用高Ti成分设计，同时严格控制S和Si的含量在较低的水平，制造出屈服强度在700MPa以上、抗拉强度在800MPa以上、延伸率在18％以上并且具有良好的耐疲劳性和成型性能的钢板。根据本发明的钢板，一方面其高强度能够满足轻量化的需要，另一方面其疲劳性能也得以大大提高。The invention provides a low-cost high-strength fatigue-resistant steel with a tensile strength of 800MPa without quenching and tempering treatment and a manufacturing method thereof. Specifically, the present invention is based on the composition of carbon-manganese structural steel, by adding an appropriate amount of microalloy elements such as Nb, V, Ti, Cr, and adopting controlled rolling and controlled cooling technology, taking into account the production characteristics of ordinary hot continuous rolling mills, Using high Ti composition design, while strictly controlling the content of S and Si at a low level, the yield strength is above 700MPa, the tensile strength is above 800MPa, the elongation is above 18%, and it has good fatigue resistance and formability performance steel. According to the steel plate of the present invention, on the one hand, its high strength can meet the requirement of light weight, and on the other hand, its fatigue performance can also be greatly improved.
根据本发明的非调质处理耐疲劳性能高的钢板，按重量百分比(％)计其化学成分为：C：0.05％～0.15％、Si≤0.1％、Mn：2.0％～2.6％、P≤0.010％、S≤0.002％、Cr：0.2％～1.0％、V：0.02％～0.1％、Ti：0.1％～0.16％、Nb：0.02％～0.06％、N≤0.004％和O≤0.002％，其余为铁Fe和不可避免的杂质，根据本发明的钢板的抗拉强度在800MPa级。根据本发明的钢板的抗拉强度在800MPa级。根据本发明的钢板，其金相组织为超细多边形铁素体和少量贝氏体，其中，多边形铁素体的体积百分比占整个金相组织的85％以上。According to the non-tempered steel plate with high fatigue resistance of the present invention, its chemical composition is calculated by weight percentage (%): C: 0.05%-0.15%, Si≤0.1%, Mn: 2.0%-2.6%, P≤ 0.010%, S≤0.002%, Cr: 0.2%～1.0%, V: 0.02%～0.1%, Ti: 0.1%～0.16%, Nb: 0.02%～0.06%, N≤0.004% and O≤0.002%, The rest is iron Fe and unavoidable impurities, and the tensile strength of the steel plate according to the present invention is at the level of 800MPa. The tensile strength of the steel sheet according to the invention is in the order of 800 MPa. According to the steel plate of the present invention, its metallographic structure is ultra-fine polygonal ferrite and a small amount of bainite, wherein the volume percentage of polygonal ferrite accounts for more than 85% of the entire metallographic structure.
根据本发明的优选实施例，根据本发明的非调质处理耐疲劳性能高的钢板，按重量百分比(％)计其化学成分为：C：0.05％～0.12％、Si≤0.1％、Mn：2.0％～2.6％、P≤0.010％、S≤0.002％、Cr：0.3％～0.8％、V：0.04％～0.08％、Ti：0.10％～0.15％、Nb：0.03％～0.06％、N≤0.004％和O≤0.002％，其余为铁Fe和不可避免的杂质。According to a preferred embodiment of the present invention, the chemical composition of the non-tempered steel plate with high fatigue resistance according to the present invention is calculated by weight percentage (%): C: 0.05% to 0.12%, Si≤0.1%, Mn: 2.0%～2.6%, P≤0.010%, S≤0.002%, Cr: 0.3%～0.8%, V: 0.04%～0.08%, Ti: 0.10%～0.15%, Nb: 0.03%～0.06%, N≤ 0.004% and O≤0.002%, the rest is iron Fe and unavoidable impurities.
下面将详细地描述根据本发明的钢板中各主要元素所起的作用。The role played by each main element in the steel sheet according to the present invention will be described in detail below.
锰(Mn)能够降低奥氏体向铁素体转变的相变温度，而奥氏体向铁素体转变的相变温度的降低对于热轧态或正火态钢材的铁素体晶粒尺寸有细化作用，因此，Mn早就作为高强度微合金钢中的主要合金元素而被广泛应用。根据本发明，考虑到本发明的钢板的性能要求，将Mn在钢中的含量限定在2.0wt％～3.0wt％。如果Mn含量过高(超过3.0wt％)，则钢板的裂纹敏感性显著增加，而如果Mn含量过低(低于2.0wt％)，则固溶强化效果不明显，从而影响强度性能。Manganese (Mn) can reduce the phase transition temperature of austenite to ferrite transformation, and the reduction of the phase transition temperature of austenite to ferrite transformation has a great influence on the ferrite grain size of hot-rolled or normalized steel Therefore, Mn has long been widely used as the main alloying element in high-strength microalloyed steel. According to the present invention, considering the performance requirements of the steel plate of the present invention, the content of Mn in the steel is limited to 2.0wt%-3.0wt%. If the Mn content is too high (more than 3.0wt%), the crack sensitivity of the steel plate will increase significantly, and if the Mn content is too low (less than 2.0wt%), the solid solution strengthening effect will not be obvious, thereby affecting the strength performance.
硅(Si)固溶于铁素体和奥氏体中，能够提高钢的强度、硬度、弹性和耐磨性。当钢中Si含量较高时，钢的焊接性能会恶化，而且Si含量高于0.1％以上将损害钢的冷弯性能。因此，在本发明中，Si在钢中的含量不超过0.1wt％。Silicon (Si) dissolves in ferrite and austenite, which can improve the strength, hardness, elasticity and wear resistance of steel. When the Si content in the steel is high, the weldability of the steel will deteriorate, and the Si content above 0.1% will damage the cold bending performance of the steel. Therefore, in the present invention, the content of Si in the steel does not exceed 0.1 wt%.
铬(Cr)可提高钢的强度和硬度以及耐磨性。将铬加入钢中能够显著改善钢的高温抗氧化性(不起皮)，显著提高钢的淬透性，并且改善钢的抗回火稳定性。另一方面，铬也能促进钢的回火脆性倾向。如果Cr含量太低，则钢的抗耐磨效果较差，而如果Cr含量较高，则会对钢的淬透性、延迟断裂性不利。因此，根据本发明，将Cr在钢中的含量限定在0.2wt％～1.0wt％，优选地限定在0.3wt％～0.8wt％。Chromium (Cr) increases the strength and hardness of steel, as well as its wear resistance. The addition of chromium to steel can significantly improve the high temperature oxidation resistance (no scaling) of steel, significantly increase the hardenability of steel, and improve the stability against tempering of steel. On the other hand, chromium can also promote the temper brittle tendency of steel. If the Cr content is too low, the anti-wear effect of the steel is poor, and if the Cr content is high, it will be unfavorable to the hardenability and delayed fracture of the steel. Therefore, according to the present invention, the content of Cr in the steel is limited to 0.2wt%-1.0wt%, preferably limited to 0.3wt%-0.8wt%.
铌(Nb)是重要的微合金化元素，可提高钢的未再结晶区温度，保障控制轧制的效果，使钢材轧制后晶粒细化，同时Nb析出的NbC沉淀粒子在轧制后期具有沉淀强化作用。如果Nb的含量太高或者太低，都会使得上述效果不明显。因此，根据本发明，将Nb在钢中的含量限定在0.02wt％～0.06wt％，优选地限定在0.03wt％～0.06wt％。Niobium (Nb) is an important microalloying element, which can increase the temperature of the non-recrystallized zone of the steel, ensure the effect of controlled rolling, and refine the grains of the steel after rolling. It has a precipitation strengthening effect. If the content of Nb is too high or too low, the above effects will not be obvious. Therefore, according to the present invention, the content of Nb in the steel is limited to 0.02wt%-0.06wt%, preferably limited to 0.03wt%-0.06wt%.
钛(Ti)是本发明中重要的沉淀强化元素，高温时析出TiN，能够有效地阻止奥氏体晶粒粗化。Ti在600℃以下，从钢中沉淀析出为纳米TiC或(Nb，Ti)C粒子，能够有效地钉扎位错，从而提高钢的屈服强度。当Ti含量少于0.08wt％时，析出沉淀强化作用不足；而当Ti含量高于0.18wt％时，会在连铸时在铸坯表面形成裂纹缺陷，同时在快速冷却的前提下，其沉淀强化作用也趋于饱和，因此，根据本发明，将Ti在钢中的含量限定在0.08wt％～0.18wt％，优选地限定在0.10wt％～0.15wt％。Titanium (Ti) is an important precipitation strengthening element in the present invention, and TiN is precipitated at high temperature, which can effectively prevent the coarsening of austenite grains. When Ti is below 600°C, it precipitates out of the steel as nano-TiC or (Nb, Ti)C particles, which can effectively pin dislocations and increase the yield strength of the steel. When the Ti content is less than 0.08wt%, the precipitation strengthening effect is insufficient; and when the Ti content is higher than 0.18wt%, crack defects will be formed on the surface of the slab during continuous casting, and at the same time, under the premise of rapid cooling, its precipitation The strengthening effect tends to be saturated, therefore, according to the present invention, the content of Ti in the steel is limited to 0.08wt%-0.18wt%, preferably 0.10wt%-0.15wt%.
钒(V)是本发明中重要的沉淀强化元素，可以选择与Nb、Ti等合金元素一起添加，以保证本发明的钢板实现800Mpa的抗拉强度。根据本发明，将V在钢中的含量限定在0.02wt％～0.1wt％，优选地限定在0.04wt％～0.08wt％。Vanadium (V) is an important precipitation-strengthening element in the present invention, which can be selected to be added together with alloying elements such as Nb and Ti to ensure that the steel plate of the present invention has a tensile strength of 800Mpa. According to the present invention, the content of V in the steel is limited to 0.02wt%-0.1wt%, preferably 0.04wt%-0.08wt%.
对于硫(S)而言，较低的S含量可以保证有害夹杂物较少的存在，大大提高钢的洁净度，从而提高钢的耐疲劳性能。因此，根据本发明，将S含量严格控制在0.002wt％以下。For sulfur (S), a lower S content can ensure the existence of less harmful inclusions, greatly improve the cleanliness of the steel, and thus improve the fatigue resistance of the steel. Therefore, according to the present invention, the S content is strictly controlled below 0.002wt%.
根据本发明的非调质处理高强耐疲劳的钢板采用以下工艺进行加工制造：转炉冶炼，精炼，连铸，连铸坯加热，热连轧，层流冷却，卷取，开卷剪切成板。即，根据本发明的钢板的制造方法可以包括冶炼工艺、轧制成型工艺及冷却和卷取工艺。在下面的描述中，为了避免冗余，省略了对与现有技术中的工艺相同的工艺的详细描述。The non-quenched and tempered high-strength fatigue-resistant steel plate of the present invention is manufactured by the following processes: converter smelting, refining, continuous casting, continuous casting slab heating, hot continuous rolling, laminar cooling, coiling, uncoiling and shearing into plates. That is, the manufacturing method of the steel plate according to the present invention may include a smelting process, a roll forming process, and a cooling and coiling process. In the following description, in order to avoid redundancy, a detailed description of the same processes as those in the related art is omitted.
下面将详细描述根据本发明的非调质处理高强耐疲劳的钢板的制造方法。The method for manufacturing the non-tempered high-strength fatigue-resistant steel plate according to the present invention will be described in detail below.
1、冶炼工艺1. Smelting process
为了精确控制Ti、Si和S等元素含量，提高钢质的洁净度，保证成型性能和疲劳性能，冶炼工艺需要实现如下操作：(1)采用预脱硫工艺，严格控制铁水S含量在0.005％以下；(2)转炉石灰采用优质活性石灰，降低S的掺杂；(3)采用滑板挡渣技术，转炉挡渣被全部挡住，转炉渣量越少越好；(4)严格控制铁水中的Si含量在0.1％以下，具体地讲，采用Al脱氧剂，降低Si的掺杂，防止Al还原SiO2而造成回Si现象的发生；(5)在对钢水合金化时，采用添加钛铁和钛线复合添加的方式，精确控制Ti的回收率和含量。In order to precisely control the content of elements such as Ti, Si and S, improve the cleanliness of the steel, and ensure the formability and fatigue performance, the smelting process needs to achieve the following operations: (1) Adopt the pre-desulfurization process and strictly control the S content of the molten iron below 0.005% ; (2) Converter lime adopts high-quality active lime to reduce the doping of S; (3) Adopt sliding plate slag blocking technology, the converter slag is completely blocked, the less the amount of converter slag, the better; (4) Strictly control Si in molten iron The content is below 0.1%. Specifically, Al deoxidizer is used to reduce the doping of Si and prevent Al from reducing SiO2 to cause the phenomenon of returning to Si; (5) when alloying molten steel, add ferro-titanium and titanium The method of line compound addition can precisely control the recovery rate and content of Ti.
通过上述措施，保证了钢中的气体含量，控制O≤30ppm、N≤50ppm、S≤0.005wt％，从而减少有害的硫化物夹杂，其中，夹杂物评级在0.5级以下。较小尺寸夹杂物的分布并且数量较少，能够提高钢质的纯净度、增加组织的均匀性并降低疲劳缺陷产生的几率，从而有效地提高钢的耐疲劳性能。Through the above measures, the gas content in the steel is guaranteed, and O≤30ppm, N≤50ppm, S≤0.005wt% are controlled, thereby reducing harmful sulfide inclusions, wherein the rating of the inclusions is below 0.5. The distribution and quantity of inclusions with smaller sizes can improve the purity of steel, increase the uniformity of structure and reduce the probability of fatigue defects, thereby effectively improving the fatigue resistance of steel.
2、轧制成型工艺2. Roll forming process
控制连铸坯的加热温度为1150℃～1250℃，加热时间达100分钟～160分钟。然后，进行控制轧制，粗轧开轧温度为1120℃～1180℃，粗轧终轧温度为1020℃～1060℃；精轧终轧温度控制在850℃～900℃，精轧过程每道次的压下量控制在15％～40％，精轧机架间采用水冷。根据本发明的优选实施例，粗轧过程可以进行3～5道次轧制，精轧过程可以进行4～6道次轧制。The heating temperature of the continuous casting slab is controlled to be 1150° C. to 1250° C., and the heating time is 100 minutes to 160 minutes. Then, controlled rolling is carried out, the rough rolling start temperature is 1120°C-1180°C, the rough rolling finish temperature is 1020°C-1060°C; the finish rolling finish temperature is controlled at 850°C-900°C. The amount of reduction is controlled at 15% to 40%, and water cooling is used between the finishing stands. According to a preferred embodiment of the present invention, the rough rolling process can be rolled for 3-5 passes, and the finish rolling process can be rolled for 4-6 passes.
3、卷取工艺及冷却工艺3. Coiling process and cooling process
对轧制后钢板采用层流冷却后进行卷取，冷却速度为5℃/s～20℃/s，卷取温度为500℃～600℃。The rolled steel plate is coiled after laminar cooling, the cooling rate is 5°C/s-20°C/s, and the coiling temperature is 500°C-600°C.
根据本发明，在合理成分设计的基础上，采用控轧控冷工艺，将加热温度控制在1150℃～1250℃，加热时间根据铸坯的冷热程度不同而适当控制在100～160分钟，这样有利于使合金元素充分地固溶；在轧制过程中，采用多道次轧制，将精轧温度的范围控制在850℃～1020℃，从而对连铸坯料在奥氏体再结晶区、未再结晶区及形变诱导相变区进行控制轧制，同时卷取温度采用500℃～600℃，能够获得最佳的析出沉淀强化效果。具体地讲，通过高温区的奥氏体再结晶区控制轧制，能够充分地细化奥氏体晶粒；通过精轧阶段的道次间水冷，降低轧件温度，能够增加奥氏体未再结晶区的变形；将精轧终轧温度控制在850～900℃，使轧制过程中产生较大的累积应变；通过轧后快速冷却及适当的卷取温度，得到超细多边形铁素体和少量贝氏体的组成。According to the present invention, on the basis of reasonable component design, the controlled rolling and controlled cooling process is adopted to control the heating temperature at 1150°C to 1250°C, and the heating time is properly controlled at 100 to 160 minutes according to the degree of coldness and heat of the slab, so that It is beneficial to fully dissolve the alloying elements; in the rolling process, multi-pass rolling is used to control the range of finishing rolling temperature at 850 ° C to 1020 ° C, so that the continuous casting billet can be treated in the austenite recrystallization zone, Controlled rolling in the non-recrystallization zone and deformation-induced phase transformation zone, and at the same time the coiling temperature is 500°C to 600°C, can obtain the best precipitation strengthening effect. Specifically, controlled rolling through the austenite recrystallization zone in the high-temperature zone can fully refine the austenite grains; through water cooling between passes in the finish rolling stage, the temperature of the rolled piece can be reduced, and the austenite recrystallization can be increased. Deformation in the recrystallization zone; control the finish rolling and finishing rolling temperature at 850-900°C, so that a large cumulative strain will be generated during the rolling process; through rapid cooling after rolling and appropriate coiling temperature, ultra-fine polygonal ferrite can be obtained and a small amount of bainite.
此外，根据本发明，根据来料的规格(厚度)不同，可以控制粗轧后的中间坯料的厚度为28mm～40mm，控制最终产品的厚度为3mm～12mm。对于轧制时的压下量和坯料的中间厚度，本领域技术人员在本发明的教导下可以根据实际需要来确定实际的轧制工艺；为了避免冗余，本发明不再对此进行描述。In addition, according to the present invention, according to the different specifications (thickness) of the incoming materials, the thickness of the intermediate billet after rough rolling can be controlled to be 28mm-40mm, and the thickness of the final product can be controlled to be 3mm-12mm. As for the rolling reduction and the middle thickness of the billet, those skilled in the art can determine the actual rolling process according to the actual needs under the teaching of the present invention; in order to avoid redundancy, the present invention will not describe this again.
以下列举具体实施例对本发明进行进一步的说明。需要指出的是，实施例只用于对本发明作进一步说明，而不代表本发明的保护范围，因此，在不脱离本发明的精神和范围的情况下，可以对本发明做出各种修改和变型。The following specific examples are given to further illustrate the present invention. It should be pointed out that the embodiments are only used to further illustrate the present invention, and do not represent the protection scope of the present invention. Therefore, without departing from the spirit and scope of the present invention, various modifications and variations can be made to the present invention .
在下面的实施例中，通过以下具体工艺流程制备各实施例的钢板：以化学成分C、Si、Mn、S、P和Fe为原料，进行电炉或者转炉冶炼，精炼过程对钢水进行合金化处理，然后进行连铸；铸坯经直接加热或者均热后，对铸坯进行粗轧和精轧；轧后采用层流水冷却坯料并进行卷取。In the following examples, the steel plates of each example are prepared through the following specific process flow: the chemical components C, Si, Mn, S, P and Fe are used as raw materials for electric furnace or converter smelting, and the molten steel is alloyed during the refining process , and then carry out continuous casting; after the billet is directly heated or soaked, rough rolling and finish rolling are carried out on the billet; after rolling, the billet is cooled by laminar flow water and coiled.
实施例1Example 1
一种高强钢，其化学成分按重量百分比为：C：0.08％、Si：0.05％、Mn：2.05％、Nb：0.042％、Ti：0.13％、V：0.02％、Cr：0.5％、P：0.008％、S：0.001％、N：0.004％、O：0.0019％，其余为铁(Fe)和不可避免的杂质。A high-strength steel, its chemical composition by weight percentage is: C: 0.08%, Si: 0.05%, Mn: 2.05%, Nb: 0.042%, Ti: 0.13%, V: 0.02%, Cr: 0.5%, P: 0.008%, S: 0.001%, N: 0.004%, O: 0.0019%, and the rest are iron (Fe) and unavoidable impurities.
将上述配制好的原料在120吨转炉上冶炼，并连铸成175mm×1210mm×11800mm的连铸坯。然后，将连铸坯加热到1230℃，加热时间160分钟，在热连轧机上轧制：粗轧开轧温度控制为1150℃，粗轧终轧温度控制为1050℃，粗轧5道次，中间坯厚为30mm；精轧开轧温度控制为1020℃，精轧终轧温度控制为850℃，精轧5道次，精轧平均每道次的压下量控制在20％，精轧机间采用水冷。将上述轧制后坯料进行层流冷却，冷却速度为18℃/s，卷取温度为600℃，最终获取高强钢带，进行开卷剪切成钢板。产品力学性能检验结果见下面的表1。The above-mentioned prepared raw materials were smelted on a 120-ton converter, and continuously cast into a continuous casting slab of 175mm×1210mm×11800mm. Then, the continuous casting slab was heated to 1230°C for a heating time of 160 minutes, and rolled on a hot continuous rolling mill: the rough rolling start temperature was controlled at 1150°C, the rough rolling finish rolling temperature was controlled at 1050°C, and the rough rolling was carried out for 5 passes. The thickness of the intermediate billet is 30mm; the temperature of the finish rolling start is controlled at 1020°C, the temperature of the finish rolling is controlled at 850°C, the finish rolling is carried out for 5 passes, and the average reduction of each pass of the finish rolling is controlled at 20%. Using water cooling. The above-mentioned billet after rolling is subjected to laminar flow cooling, the cooling rate is 18°C/s, and the coiling temperature is 600°C, and finally a high-strength steel strip is obtained, which is uncoiled and sheared into steel plates. The test results of the mechanical properties of the product are shown in Table 1 below.
实施例2Example 2
一种高强钢，其化学成分按重量百分比为：C：0.07％、Si：0.03％、Mn：2.25％、Nb：0.06％、Ti：0.15％、V：0.04％、Cr：0.8％、N：0.0038％、O：0.002％、P：0.008％和S：0.002％，其余为铁(Fe)和不可避免的杂质。A high-strength steel, its chemical composition by weight percentage is: C: 0.07%, Si: 0.03%, Mn: 2.25%, Nb: 0.06%, Ti: 0.15%, V: 0.04%, Cr: 0.8%, N: 0.0038%, O: 0.002%, P: 0.008%, and S: 0.002%, and the rest are iron (Fe) and unavoidable impurities.
将上述配制好的原料在120吨转炉上冶炼，并连铸成175mm×1230mm×11800mm的连铸坯。然后，将连铸坯加热到1250℃，加热时间150分钟，在热连轧机上轧制：粗轧开轧温度控制为1180℃，粗轧终轧温度控制为1060℃，粗轧5道次，中间坯厚度为28mm；接着对中间坯进行精轧，精轧开轧温度控制为1040℃，精轧终轧温度控制为880℃，精轧6道次，精轧平均每道次的压下量控制在35％，精轧机间采用水冷。然后，将上述轧制后的坯料进行层流冷却，冷却速度为22℃/S，卷取温度为550℃，最终获取高强钢带，进行开卷剪切成钢板。产品力学性能检验结果见下面的表1。The above-mentioned prepared raw materials were smelted on a 120-ton converter, and continuously cast into a continuous casting slab of 175mm×1230mm×11800mm. Then, the continuous casting slab was heated to 1250°C for a heating time of 150 minutes, and rolled on a hot continuous rolling mill: the rough rolling start temperature was controlled at 1180°C, the rough rolling finish rolling temperature was controlled at 1060°C, and the rough rolling was carried out for 5 passes. The thickness of the intermediate slab is 28mm; then the intermediate slab is finished rolling, the temperature of the start of the finish rolling is controlled at 1040°C, the temperature of the finish rolling is controlled at 880°C, and the finish rolling is carried out 6 times, and the average reduction of each pass of the finish rolling is It is controlled at 35%, and water cooling is adopted between the finishing mills. Then, laminar cooling is carried out on the above-mentioned billet after rolling, the cooling rate is 22°C/S, and the coiling temperature is 550°C, and finally a high-strength steel strip is obtained, which is uncoiled and sheared into steel plates. The test results of the mechanical properties of the product are shown in Table 1 below.
实施例3Example 3
一种高强钢，其化学成分按重量百分比为：C：0.05％、Si：0.07％、Mn：3.0％、Nb：0.048％、Ti：0.18％、V：0.05％、Cr：0.2％、N：0.038％、O：0.020％、P：0.005％和S：0.015％，其余为铁(Fe)和不可避免的杂质。A high-strength steel, its chemical composition by weight percentage is: C: 0.05%, Si: 0.07%, Mn: 3.0%, Nb: 0.048%, Ti: 0.18%, V: 0.05%, Cr: 0.2%, N: 0.038%, O: 0.020%, P: 0.005%, and S: 0.015%, and the rest are iron (Fe) and unavoidable impurities.
将上述配制好的原料在120吨转炉上冶炼，并连铸成175mm×1230mm×11800mm的连铸坯。然后，将连铸坯加热到1150℃，加热时间100分钟，在热连轧机上轧制：粗轧开轧温度控制为1120℃，粗轧终轧温度控制为1040℃，粗轧5道次，中间坯厚度为40mm；接着对中间坯进行精轧，精轧开轧温度控制为1000℃，精轧终轧温度控制为850℃，精轧5道次，精轧平均每道次的压下量控制在15％，精轧机间采用水冷。然后，将上述轧制后的坯料进行层流冷却，冷却速度为15℃/S，卷取温度为530℃，最终获取高强钢带，进行开卷剪切成钢板。产品力学性能检验结果见下面的表1。The above-mentioned prepared raw materials were smelted on a 120-ton converter, and continuously cast into a continuous casting slab of 175mm×1230mm×11800mm. Then, the continuous casting slab is heated to 1150°C, the heating time is 100 minutes, and rolled on a hot continuous rolling mill: the rough rolling start temperature is controlled at 1120°C, the rough rolling finish rolling temperature is controlled at 1040°C, and the rough rolling is carried out for 5 passes. The thickness of the intermediate slab is 40mm; then the intermediate slab is finished rolling, the temperature of the start rolling of the finish rolling is controlled at 1000°C, the temperature of the finish rolling is controlled at 850°C, the finish rolling is carried out for 5 passes, and the average reduction of each pass of the finish rolling is It is controlled at 15%, and water cooling is adopted between the finishing mills. Then, laminar cooling is carried out on the above-mentioned billet after rolling, the cooling rate is 15°C/S, and the coiling temperature is 530°C, and finally a high-strength steel strip is obtained, which is uncoiled and sheared into steel plates. The test results of the mechanical properties of the product are shown in Table 1 below.
实施例4Example 4
一种高强钢，其化学成分按重量百分比为：C：0.12％、Si：0.1％、Mn：2.0％、Nb：0.02％、Ti：0.08％、V：0.08％、Cr：0.3％、N：0.038％、O：0.020％、P：0.010％和S：0.002％，其余为铁(Fe)和不可避免的杂质。A high-strength steel, its chemical composition by weight percentage is: C: 0.12%, Si: 0.1%, Mn: 2.0%, Nb: 0.02%, Ti: 0.08%, V: 0.08%, Cr: 0.3%, N: 0.038%, O: 0.020%, P: 0.010%, and S: 0.002%, and the rest are iron (Fe) and unavoidable impurities.
将上述配制好的原料在120吨转炉上冶炼，并连铸成175mm×1230mm×11800mm的连铸坯。然后，将连铸坯加热到1180℃，加热时间140分钟，在热连轧机上轧制：粗轧开轧温度控制为1170℃，粗轧终轧温度控制为1020℃，粗轧5道次，中间坯厚度为36mm；接着对中间坯进行精轧，精轧开轧温度控制为1000℃，精轧终轧温度控制为850℃，精轧4道次，精轧平均每道次的压下量控制在30％，精轧机间采用水冷。然后，将上述轧制后的坯料进行层流冷却，冷却速度为18℃/S，卷取温度为530℃，最终获取高强钢带，进行开卷剪切成钢板。产品力学性能检验结果见下面的表1。The above-mentioned prepared raw materials were smelted on a 120-ton converter, and continuously cast into a continuous casting slab of 175mm×1230mm×11800mm. Then, the continuous casting slab was heated to 1180°C for a heating time of 140 minutes, and rolled on a hot continuous rolling mill: the rough rolling start temperature was controlled at 1170°C, the rough rolling finish rolling temperature was controlled at 1020°C, and the rough rolling was carried out for 5 passes. The thickness of the intermediate slab is 36mm; then the intermediate slab is finished rolling, the temperature of the start rolling of the finish rolling is controlled at 1000°C, the temperature of the finish rolling is controlled at 850°C, and the finish rolling is carried out 4 times, and the average reduction of each pass of the finish rolling is It is controlled at 30%, and water cooling is adopted between the finishing mills. Then, laminar cooling is carried out on the above-mentioned billet after rolling, the cooling rate is 18°C/S, and the coiling temperature is 530°C, and finally a high-strength steel strip is obtained, which is uncoiled and sheared into steel plates. The test results of the mechanical properties of the product are shown in Table 1 below.
实施例5Example 5
一种高强钢，其化学成分按重量百分比为：C：0.15％、Si：0.03％、Mn：2.6％、Nb：0.03％、Ti：0.10％、V：0.1％、Cr：1.0％、N：0.0035％、O：0.001％、P：0.008％和S：0.002％，其余为铁(Fe)和不可避免的杂质。A high-strength steel, its chemical composition by weight percentage is: C: 0.15%, Si: 0.03%, Mn: 2.6%, Nb: 0.03%, Ti: 0.10%, V: 0.1%, Cr: 1.0%, N: 0.0035%, O: 0.001%, P: 0.008%, and S: 0.002%, and the rest are iron (Fe) and unavoidable impurities.
将上述配制好的原料在120吨转炉上冶炼，并连铸成175mm×1230mm×11800mm的连铸坯。然后，将连铸坯加热到1250℃，加热时间150分钟，在热连轧机上轧制：粗轧开轧温度控制为1180℃，粗轧终轧温度控制为1060℃，粗轧5道次，中间坯厚度为38mm；接着对中间坯进行精轧，精轧开轧温度控制为1040℃，精轧终轧温度控制为880℃，精轧5道次，精轧平均每道次的压下量控制在35％，精轧机间采用水冷。然后，将上述轧制后的坯料进行层流冷却，冷却速度为22℃/S，卷取温度为550℃，最终获取高强钢带，进行开卷剪切成钢板。产品力学性能检验结果见下面的表1。The above-mentioned prepared raw materials were smelted on a 120-ton converter, and continuously cast into a continuous casting slab of 175mm×1230mm×11800mm. Then, the continuous casting slab was heated to 1250°C for a heating time of 150 minutes, and rolled on a hot continuous rolling mill: the rough rolling start temperature was controlled at 1180°C, the rough rolling finish rolling temperature was controlled at 1060°C, and the rough rolling was carried out for 5 passes. The thickness of the intermediate slab is 38mm; then the intermediate slab is finished rolling, the temperature of the start rolling of the finish rolling is controlled at 1040°C, the temperature of the finish rolling is controlled at 880°C, the finish rolling is carried out for 5 passes, and the average reduction of each pass of the finish rolling is It is controlled at 35%, and water cooling is adopted between the finishing mills. Then, laminar cooling is carried out on the above-mentioned billet after rolling, the cooling rate is 22°C/S, and the coiling temperature is 550°C, and finally a high-strength steel strip is obtained, which is uncoiled and sheared into steel plates. The test results of the mechanical properties of the product are shown in Table 1 below.
表1实施例1至5的钢板的性能The performance of the steel plate of table 1 embodiment 1 to 5
在上面的表1中，Rel指屈服强度，Rm指抗拉强度，δ指延伸率。In Table 1 above, Rel refers to yield strength, Rm refers to tensile strength, and δ refers to elongation.
通过上面的表1可知，采用本发明的方法，能够使钢板具有高的抗拉强度，达800MPa以上。将实施例1至5所得的钢板在PLG-100C高频疲劳试验机上进行测试，加载方式为轴向动载，采用升降法测量材料在N＝107周时的条件疲劳极限，频率约为92Hz。测定结果表明，实施例1的钢板的条件疲劳极限为815MPa，实施例2的钢板的疲劳极限为810MPa，实施例3的钢板的疲劳极限为802MPa，实施例4的钢板的疲劳极限为803MPa，实施例5的钢板的疲劳极限为800MPa。It can be known from the above Table 1 that the method of the present invention can make the steel plate have high tensile strength, which can reach more than 800 MPa. The steel plates obtained in Examples 1 to 5 are tested on a PLG-100C high-frequency fatigue testing machine, the loading method is axial dynamic load, and the conditional fatigue limit of the material is measured at N=10 7 weeks by the lifting method, and the frequency is about 92Hz . Measured result shows, the conditional fatigue limit of the steel plate of embodiment 1 is 815MPa, the fatigue limit of the steel plate of embodiment 2 is 810MPa, the fatigue limit of the steel plate of embodiment 3 is 802MPa, the fatigue limit of the steel plate of embodiment 4 is 803MPa, implement The fatigue limit of the steel plate of Example 5 was 800 MPa.
由以上试验结果可以表明，根据本发明的方法在提高钢板的强度的同时，能够使钢板具备良好的耐疲劳性能，从而根据本发明的钢板能够满足工程机械和汽车结构钢用户的使用的要求。It can be shown from the above test results that according to the method of the present invention, the steel plate can be provided with good fatigue resistance while improving the strength of the steel plate, so that the steel plate according to the present invention can meet the requirements of construction machinery and automobile structural steel users.
本发明与已有技术相比较，具有下列显著的优点和效果：Compared with the prior art, the present invention has the following remarkable advantages and effects:
1)本发明采用特殊的冶炼工艺，通过提高钢水纯净度，减小了裂纹产生的几率，提高了钢的疲劳性能。而且，本发明用较高的Cr含量代替高成本的合金元素Mo等，通过细晶强化和沉淀强化作用，使得抗拉强度达到了800MPa以上。另外，在本发明的钢板中，Si≤0.1％和S≤0.005％，有助于提高成型性能和耐疲劳性能。1) The present invention adopts a special smelting process to reduce the probability of cracks and improve the fatigue performance of steel by improving the purity of molten steel. Moreover, the present invention replaces high-cost alloying elements Mo and the like with relatively high Cr content, and through fine-grain strengthening and precipitation strengthening, the tensile strength reaches more than 800 MPa. In addition, in the steel sheet of the present invention, Si≤0.1% and S≤0.005%, contribute to the improvement of formability and fatigue resistance.
2)根据本发明的钢板的强度高，根据不同的厚度规格，屈服强度达700MPa～780MPa，抗拉强度达800MPa～960MPa，延伸率达18％～30％。2) The steel plate according to the present invention has high strength. According to different thickness specifications, the yield strength reaches 700MPa-780MPa, the tensile strength reaches 800MPa-960MPa, and the elongation reaches 18%-30%.
3)根据本发明的钢板的耐疲劳性能好，条件疲劳极限在800Mpa以上。3) The steel plate according to the present invention has good fatigue resistance, and the conditional fatigue limit is above 800Mpa.
4)根据本发明的钢板具有超细化的多边形铁素体组织，使材料具有较高的屈服强度良好的塑性，同时材料的韧性得到提高；而且，适量的贝氏体可有效地提高抗拉强度，改善加工硬化能力，降低屈强比，使材料在提高强度的同时，还具有良好的冷成型性。4) The steel plate according to the present invention has an ultra-fine polygonal ferrite structure, so that the material has a higher yield strength and good plasticity, and the toughness of the material is improved at the same time; and an appropriate amount of bainite can effectively improve the tensile strength. Strength, improve work hardening ability, reduce yield ratio, so that the material has good cold formability while improving strength.
5)根据本发明，将卷取温度控制在500℃～600℃，有利于得到贝氏体组织，提高强度，而且与现有技术的低温卷取相比，在本发明中更加易于控制卷取工艺。5) According to the present invention, the coiling temperature is controlled at 500°C to 600°C, which is beneficial to obtain the bainite structure and improve the strength, and compared with the low-temperature coiling of the prior art, it is easier to control the coiling in the present invention craft.
本发明不限于上述实施例，在不脱离本发明的精神和范围的情况下，可以对本发明的实施例进行各种变型和修改。The present invention is not limited to the above-described embodiments, and various variations and modifications can be made to the embodiments of the present invention without departing from the spirit and scope of the present invention.
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