CN114107835A

CN114107835A - 1180 MPa-grade high-plasticity high-hole-expansion steel and manufacturing method thereof

Info

Publication number: CN114107835A
Application number: CN202010897941.5A
Authority: CN
Inventors: 王焕荣; 杨峰; 张晨; 杨阿娜
Original assignee: Baoshan Iron and Steel Co Ltd
Current assignee: Baoshan Iron and Steel Co Ltd
Priority date: 2020-08-31
Filing date: 2020-08-31
Publication date: 2022-03-01

Abstract

A1180 MPa grade high plasticity high reaming steel and a manufacturing method thereof comprise the following chemical components in percentage by weight: 0.06-0.10% of C, 0.8-2.0% of Si, 1.5-2.0% of Mn, less than or equal to 0.02% of P, less than or equal to 0.003% of S, 0.02-0.08% of Al, less than or equal to 0.004% of N, 0.1-0.5% of Mo, 0.01-0.05% of Ti, less than or equal to 0.0030% of O, and the balance of Fe and other inevitable impurities. The yield strength of the high-hole-expansion steel is more than or equal to 900MPa, the tensile strength is more than or equal to 1180MPa, and the elongation (in the transverse direction A) is₅₀Not less than 10 percent) and the hole expanding rate not less than 30 percent, can be applied to parts needing high strength thinning, such as control arms, auxiliary frames and the like, of the chassis of the passenger car.

Description

1180 MPa-grade high-plasticity high-hole-expansion steel and manufacturing method thereof

Technical Field

The invention relates to the field of high-strength steel, in particular to 1180MPa grade high-plasticity high-hole-expansion steel and a manufacturing method thereof.

Background

With the development of national economy, the production of automobiles is greatly increased, and the use amount of plates is continuously increased. The original design requirements of parts of many vehicle types in the domestic automobile industry require the use of hot-rolled or pickled plates, such as chassis parts, torsion beams, auxiliary frames of cars, wheel spokes and rims, front and rear axle assemblies, body structural parts, seats, clutches, safety belts, truck box plates, protective nets, automobile girders and other parts of automobiles. Wherein, the proportion of the chassis steel to the total steel used by the car can reach 24 to 34 percent.

The light weight of passenger cars is not only a development trend in the automotive industry, but also a requirement of legal regulations. The fuel consumption is regulated by laws and regulations, the weight of a vehicle body is required to be reduced in a phase-changing manner, and the requirement reflected on materials is high strength, thinning and light weight. High strength subtracts heavy is the inevitable requirement of follow-up new motorcycle type, and this must lead to the fact with the steel grade higher, also must bring the change on the chassis structure: if the parts are more complex, the requirements on material performance, surface and the like and the forming technology are improved, such as hydraulic forming, hot stamping, laser welding and the like, and the performances of high strength, stamping, flanging, resilience, fatigue and the like of the material are further converted.

Compared with the foreign countries, the development of domestic high-strength high-hole-expansion steel has relatively lower strength level and poor performance stability. For example, high-expansion-hole steel used by domestic automobile part enterprises is basically high-strength steel with the tensile strength of below 600MPa, and high-expansion-hole steel with the tensile strength of below 440MPa competes for whitening. High hole expansion steel with 780 MPa-grade tensile strength is gradually used in batch at present, but higher requirements are provided for two important indexes of forming elongation and hole expansion rate. And 980 MPa-grade high-reaming steel is still in a research and development certification stage at present and does not reach a batch use stage. High hole expansion steel with higher strength grade such as 1180MPa has not been developed by manufacturers. Based on the development trend of high-hole-expansion steel, in order to better meet the potential requirements of users, 1180MPa high-hole-expansion steel with higher strength level needs to be developed.

The documents related to 980MPa grade high-hole-expansion steel are few, and 1180MPa grade high-hole-expansion steel is blank. Most of the related patent documents are high-hole-expansion steels of 780MPa or less. A large number of researches indicate that the elongation rate of the material is in inverse proportion to the hole expansion rate, namely the higher the elongation rate is, the lower the hole expansion rate is; conversely, the lower the elongation, the higher the hole expansion ratio. Also, the higher the strength of the material, the lower the hole expansion ratio. In order to obtain a steel material having good plasticity and hole-enlarging and flanging performance, the relationship between the two needs to be better balanced. A single homogeneous structure is advantageous for achieving higher porosities, whereas a bi-or multiphase structure is generally disadvantageous for increasing the porosities.

Disclosure of Invention

The invention aims to provide 1180MPa grade high-plasticity high-hole-expansion steel and a manufacturing method thereof, wherein the yield strength of the high-hole-expansion steel is more than or equal to 900MPa, the tensile strength of the high-hole-expansion steel is more than or equal to 1180MPa, and the elongation (transverse A) of the high-hole-expansion steel is₅₀Not less than 10 percent) and the hole expanding rate not less than 30 percent, can be applied to parts needing high strength thinning, such as control arms, auxiliary frames and the like, of the chassis of the passenger car.

In order to achieve the purpose, the technical scheme of the invention is as follows:

the high-reaming steel disclosed by the invention adopts a lower C content in component design, so that excellent weldability is ensured when a user uses the high-reaming steel, and the obtained martensite structure has good reaming performance and impact toughness; designing higher Si content, and matching with the process to obtain more residual austenite, thereby improving the plasticity of the material; meanwhile, in the process of cover retreat, the aims of improving the uniformity of the structure and improving the plasticity and the hole expansion rate can be fulfilled by eliminating part of quenching stress.

Specifically, the 1180MPa grade high plasticity high hole expansion steel comprises the following chemical components in percentage by weight: 0.06-0.10% of C, 0.8-2.0% of Si, 1.5-2.0% of Mn, less than or equal to 0.02% of P, less than or equal to 0.003% of S, 0.02-0.08% of Al, less than or equal to 0.004% of N, 0.1-0.5% of Mo, 0.01-0.05% of Ti, less than or equal to 0.0030% of O, and the balance of Fe and other inevitable impurities.

Further, the alloy also comprises one or more elements of Cr less than or equal to 0.5 percent, B less than or equal to 0.002 percent, Ca less than or equal to 0.005 percent, Nb less than or equal to 0.06 percent, V less than or equal to 0.05 percent, Cu less than or equal to 0.5 percent and Ni less than or equal to 0.5 percent, wherein the content of Cr is preferably 0.2 to 0.4 percent, and the content of Cu and Ni is preferably less than or equal to 0.3 percent respectively; the content of Nb and V is preferably less than or equal to 0.03 percent respectively; the content of B is preferably 0.0005-0.0015%, and the content of Ca is preferably 0.002% or less.

In the composition design of the high hole expansion steel of the invention:

carbon is an essential element in steel and is also one of the important elements in the present invention. Carbon expands the austenite phase region and stabilizes austenite. Carbon, which is an interstitial atom in steel, plays a very important role in increasing the strength of steel, and has the greatest influence on the yield strength and tensile strength of steel. In the invention, because the obtained structure is single-phase tempered martensite, in order to obtain high-strength steel with the final tensile strength reaching 1180MPa, the content of carbon is required to be ensured to be more than 0.06 percent, otherwise, the content of carbon is less than 0.06 percent, and the tensile strength can not reach 1180MPa even if the steel is completely quenched to room temperature; but the carbon content cannot be higher than 0.10%. The carbon content is too high, the strength of the formed low-carbon martensite is too high, and the carbide formed in the structure after the covering and withdrawing is too much, so that the elongation and the hole expansibility are not favorable. Therefore, the carbon content should be controlled to be between 0.06-0.10%, and preferably in the range of 0.07-0.09%.

Silicon is an essential element in steel and is also one of the important elements in the present invention. The Si content is increased, so that the solid solution strengthening effect is improved, and more importantly, the following two effects are achieved. Firstly, the non-recrystallization temperature of the steel is greatly reduced, and the dynamic recrystallization of the steel can be completed in a very low temperature range. Therefore, in the actual rolling process, rolling can be carried out at a relatively low finish rolling temperature, for example, rolling is carried out within the finish rolling temperature range of 800-850 ℃, so that the grain size of austenite can be greatly reduced, the final size of a martensite lath is reduced, the strength and the plasticity are favorably improved, and meanwhile, good hole expansion rate is favorably obtained; the other important function of Si is to inhibit cementite precipitation, and a certain amount of retained austenite can be reserved under proper rolling process conditions, especially when a structure mainly comprising martensite is obtained, so that the elongation is favorably improved. It is known that the elongation of martensite is usually the lowest under the same strength class conditions, and that retention of a certain amount of stable retained austenite is an important measure in order to increase the elongation of martensite. This effect of Si must be exhibited when its content reaches 0.8% or more; but the content of Si is not too high, otherwise, the rolling force load is too large in the actual rolling process, and the stable production of products is not facilitated. Therefore, the Si content in the steel is usually controlled to be between 0.8 and 2.0%, and preferably in the range of 1.0 to 1.4%.

Manganese is also the most basic element in steel and is one of the most important elements in the present invention. It is known that Mn is an important element for expanding the austenite phase region, and can reduce the critical quenching rate of steel, stabilize austenite, refine grains, and delay transformation of austenite to pearlite. In the invention, in order to ensure the strength of the steel plate and stabilize the retained austenite, the content of Mn is generally controlled to be more than 1.5%; meanwhile, the Mn content is generally not more than 2.0%, otherwise Mn segregation is likely to occur during steel making, and hot cracking is also likely to occur during slab continuous casting. Therefore, the Mn content in the steel is generally controlled to 1.5 to 2.0%, preferably in the range of 1.6 to 1.9%.

Phosphorus, an impurity element in steel. P is easy to be partially gathered on the grain boundary, and Fe is formed when the content of P in steel is higher (more than or equal to 0.1 percent)₂P is precipitated around the crystal grains to reduce the plasticity and toughness of the steel, so the lower the content, the better the controlThe steel is better within 0.02 percent without increasing the steel-making cost.

Sulfur is an impurity element in steel. S in steel is usually combined with Mn to form MnS inclusions, and particularly when the contents of S and Mn are high, the steel forms more MnS, and the MnS has certain plasticity, and the MnS deforms along the rolling direction in the subsequent rolling process, so that the transverse plasticity of the steel is reduced, the structural anisotropy is increased, and the hole expansion performance is not favorable. Therefore, the lower the S content in the steel, the better, considering that the Mn content in the present invention must be at a high level, the S content is strictly controlled in order to reduce the MnS content, and the S content is required to be controlled to be within 0.003%, and preferably to be within 0.0015%.

The role of aluminum in steel is mainly deoxidation and nitrogen fixation. In the presence of strong carbide forming elements such as Ti, Nb, V, etc., Al mainly functions to deoxidize and refine grains. In the invention, Al is taken as a common deoxidizing element and an element for refining grains, and the content of Al is usually controlled to be 0.02-0.08%; the Al content is lower than 0.02 percent, and the effect of refining grains is not achieved; similarly, when the Al content is higher than 0.08%, the effect of refining grains is saturated. Therefore, the Al content in the steel may be controlled to be 0.02 to 0.08%, and preferably 0.02 to 0.05%.

Nitrogen belongs to impurity elements in the present invention, and the lower the content, the better. Nitrogen is an unavoidable element in the steel making process. Although the content thereof is small, the formed TiN particles, in combination with a strong carbide forming element such as Ti or the like, have a very adverse effect on the properties of the steel, particularly on the hole expansibility. Because TiN is square, great stress concentration exists between the sharp corner and the substrate, and cracks are easily formed by the stress concentration between the TiN and the substrate in the reaming deformation process, so that the reaming performance of the material is greatly reduced. On the premise of controlling the nitrogen content as much as possible, the lower the content of the element forming strong carbide such as Ti, the better. In the present invention, a trace amount of Ti is added to fix nitrogen, and the adverse effect of TiN is minimized. Therefore, the nitrogen content should be controlled to 0.004% or less, and preferably 0.003% or less.

Titanium is one of important elements in the present invention. Ti plays two main roles in the present invention: firstly, the nitrogen-fixing agent is combined with impurity element N in steel to form TiN, and plays a part of the role of nitrogen fixation; secondly, a certain amount of TiN with fine dispersion is formed in the subsequent welding process of the material, thereby inhibiting the size of austenite grains, refining the structure and improving the low-temperature toughness. Therefore, the Ti content in the steel is controlled in the range of 0.01 to 0.05%, and preferably in the range of 0.01 to 0.03%.

Molybdenum, is one of the important elements in the present invention. The addition of molybdenum to the steel can greatly retard ferrite and pearlite transformation. The effect of the molybdenum is beneficial to adjusting various processes in the actual rolling process, such as sectional cooling after finishing the final rolling, air cooling before water cooling and the like. In the invention, a process of air cooling and then water cooling or direct water cooling after rolling is adopted, the addition of molybdenum can ensure that structures such as ferrite or pearlite and the like cannot be formed in the air cooling process, and meanwhile, deformed austenite can be dynamically restored in the air cooling process, thereby being beneficial to improving the uniformity of the structures; molybdenum has strong resistance to solder softening. Because the invention mainly aims to obtain the structure of single low-carbon martensite and a small amount of residual austenite, the low-carbon martensite is easy to soften after welding, and the addition of a certain amount of molybdenum can effectively reduce the softening degree of welding. Therefore, the content of molybdenum should be controlled between 0.1-0.5%, preferably in the range of 0.15-0.35%.

Chromium is one of the elements that can be added in the present invention. The addition of a small amount of chromium element is not for improving the hardenability of the steel, but for combining with B, which is beneficial to forming an acicular ferrite structure in a welding heat affected zone after welding, and can greatly improve the low-temperature toughness of the welding heat affected zone. Since the final application parts related by the invention are passenger car chassis products, the low-temperature toughness of the welding heat affected zone is an important index. Besides ensuring that the strength of the welding heat affected zone cannot be reduced too much, the low-temperature toughness of the welding heat affected zone also meets certain requirements. In addition, chromium itself has some resistance to solder softening. Therefore, the addition amount of chromium in the steel is generally less than or equal to 0.5%, and the preferable range is 0.2-0.4%.

Boron is one of the elements that can be added in the present invention. Boron mainly has the function of being segregated at the original austenite grain boundary in the steel and inhibiting the formation of proeutectoid ferrite; boron added to steel can also greatly improve the hardenability of steel. However, in the present invention, the trace amount of boron is added not mainly for the purpose of enhancing hardenability but for the purpose of improving the structure of the weld heat affected zone in combination with chromium to obtain an acicular ferrite structure having good toughness. The addition of boron in the steel is generally controlled below 0.002%, and the preferred range is 0.0005-0.0015%.

Calcium, an added element in the present invention. Calcium can improve the form of sulfides such as MnS, so that elongated sulfides such as MnS and the like are changed into spherical CaS, the inclusion form is favorably improved, the adverse effect of the elongated sulfides on the hole expanding performance is further reduced, but the addition of excessive calcium can increase the amount of calcium oxide, and is adverse to the hole expanding performance. Therefore, the addition amount of calcium in steel grades is usually less than or equal to 0.005%, and the preferable range is less than or equal to 0.002%.

Oxygen, which is an inevitable element in the steel making process, is an essential element in the present invention, and the content of O in steel after deoxidation is generally 30ppm or less, and does not cause significant adverse effects on the properties of the steel sheet. Therefore, the O content in the steel is controlled to be within 30 ppm.

Niobium, is one of the elements that may be added in the present invention. Niobium is similar to titanium and is a strong carbide element in steel, niobium is added into the steel to greatly improve the non-recrystallization temperature of the steel, deformed austenite with higher dislocation density can be obtained in the finish rolling stage, and the final phase change structure can be refined in the subsequent transformation process. However, the addition amount of niobium is not so large that the addition amount of niobium exceeds 0.06%, which tends to form relatively coarse carbonitrides of niobium in the microstructure, consume part of carbon atoms, and reduce the precipitation strengthening effect of carbides. Meanwhile, the niobium content is high, the anisotropy of hot-rolled austenite structures is easily caused, and the anisotropy is transmitted to final structures in the subsequent cooling phase change process, so that the reaming performance is not good. Therefore, the niobium content in the steel is usually controlled to 0.06% or less, and preferably in the range of 0.03% or less.

Vanadium, is an additive element in the present invention. Vanadium, like titanium and niobium, is also a strong carbide former. However, vanadium carbides are low in solid solution or precipitation temperature, and are usually all solid-dissolved in austenite in the finish rolling stage. Only when the temperature is lowered to start the phase transformation does vanadium start to form in the ferrite. Because the solid solubility of vanadium carbide in ferrite is larger than that of niobium and titanium, the vanadium carbide has larger size in ferrite, is not beneficial to precipitation strengthening and contributes far less to the strength of steel than titanium, but because certain carbon atoms are consumed in the formation of vanadium carbide, the steel strength is not beneficial to improvement. Therefore, the amount of vanadium added to the steel is usually 0.05% or less, preferably 0.03% or less.

Copper, which is an additive element in the present invention. The corrosion resistance of the steel can be improved by adding the copper into the steel, and the corrosion resistance effect is better when the copper and the P element are added together; when the addition amount of Cu exceeds 1%, an epsilon-Cu precipitated phase can be formed under certain conditions, and a strong precipitation strengthening effect is achieved. However, addition of Cu is likely to cause the phenomenon of "Cu embrittlement" during rolling, and in order to fully utilize the effect of Cu on improving corrosion resistance in some applications without causing significant "Cu embrittlement", the content of Cu element is usually controlled to be within 0.5%, preferably within 0.3%.

Nickel, which is an additive element in the present invention. The nickel added into the steel has certain corrosion resistance, but the corrosion resistance effect is weaker than that of copper, the nickel added into the steel has little influence on the tensile property of the steel, but the structure and the precipitated phase of the steel can be refined, and the low-temperature toughness of the steel is greatly improved; meanwhile, in the steel added with copper element, a small amount of nickel is added to inhibit the generation of Cu brittleness. The addition of higher nickel has no significant adverse effect on the properties of the steel itself. If copper and nickel are added simultaneously, not only can the corrosion resistance be improved, but also the structure and precipitated phase of the steel are refined, and the low-temperature toughness is greatly improved. However, both copper and nickel are relatively expensive alloying elements. Therefore, in order to minimize the cost of alloy design, the amount of nickel added is usually 0.5% or less, preferably 0.3% or less.

The invention relates to a manufacturing method of 1180MPa grade high-plasticity high-hole-expansion steel, which comprises the following steps of:

1) smelting and casting

Smelting the components by a converter or an electric furnace, secondarily refining the components by a vacuum furnace, and then casting the components into a casting blank or an ingot;

2) the casting blank or the cast ingot is heated again at the temperature of 1100 ℃ and 1200 ℃, and the heat preservation time is 1-2 hours;

3) hot rolling

The initial rolling temperature: at 950-1100 ℃, under 3-5 times of large pressure above 950 ℃, the accumulated deformation is more than or equal to 50 percent; then rolling for 3-7 passes and the accumulated deformation is more than or equal to 70 percent; the finishing temperature is 800 ℃ and 950 ℃;

4) cooling down

Firstly, air cooling is carried out for 0-10s, and then the strip steel is cooled to room temperature by water at a cooling speed of more than or equal to 30 ℃/s and then coiled;

5) annealing

Cover annealing is adopted, the heating speed is more than or equal to 20 ℃/h, the cover annealing temperature is 100-; cooling the steel plate to below 100 ℃ at a cooling speed of less than or equal to 50 ℃/h, and discharging;

6) acid pickling

The pickling operation speed of the strip steel can be adjusted within the range of 30-90 m/min, the pickling temperature is controlled within the range of 75-85 ℃, the withdrawal and straightening rate is controlled to be less than or equal to 1.5% so as to reduce the elongation loss of the strip steel, and then the strip steel is rinsed, dried on the surface of the strip steel and oiled.

Preferably, after the acid cleaning in the step 6), rinsing is carried out at the temperature range of 35-50 ℃, and the surface of the strip steel is dried and oiled at the temperature of 120-140 ℃.

The innovation points of the invention are as follows:

In the invention, on the aspect of structure design, a low-carbon tempered martensite design idea is adopted, and higher silicon is added to inhibit and reduce the formation of cementite and simultaneously reduce the non-recrystallization temperature; the austenite can be stabilized by adopting higher manganese; while a certain amount of molybdenum can greatly delay ferrite and pearlite transformation. Relatively low finishing temperature and on-line quenching after rolling are adopted, original austenite grains with fine, uniform and equiaxial grains can be obtained, and low-carbon martensite and retained austenite with uniform tissues are finally obtained. The retained austenite endows the steel plate with higher plasticity and cold bending property, the martensite endows the steel plate with high strength, and the uniform and fine structure endows the steel plate with higher hole expansion property and low-temperature toughness.

In the design of the rolling process, the rhythm of the rolling process is required to be completed as fast as possible in the stages of rough rolling and finish rolling. After finishing rolling, air cooling is firstly carried out for a certain time. The main purposes of air cooling are as follows: because of the higher manganese and molybdenum content in the composition design, the manganese is an element for stabilizing austenite, and the molybdenum greatly delays ferrite and pearlite phase transformation. Therefore, during the air-cooling for a certain period of time, the rolled deformed austenite does not undergo phase transformation, i.e., ferrite structure, but dynamic recrystallization and relaxation processes. Dynamic recrystallization of the deformed austenite can form nearly equiaxial austenite with uniform structure, dislocation in austenite grains can be greatly reduced after relaxation, and the two can be combined to obtain martensite with uniform structure in the subsequent water-cooling quenching process; the final rolling can be directly quenched to room temperature in an online manner. In order to obtain a martensite structure, the water cooling speed is higher than the critical cooling speed of the low-carbon martensite, and in the invention, the water cooling speed of the strip steel is required to be more than or equal to 30 ℃/s in order to ensure that the martensite can be obtained by all component designs.

Because the microstructure involved in the invention is low-carbon tempered martensite, the steel strip can be cooled to room temperature at a cooling speed higher than the critical cooling speed after finishing rolling, and the cover annealing temperature and time are controlled within a certain range in the subsequent cover annealing process, so that the ultrahigh-strength hole-expanding steel with uniform properties such as strength, plasticity, hole expansion and the like can be obtained.

The cover retreating temperature and the cover retreating time are in an inverse relation, namely the lower the cover retreating temperature is, the longer the cover retreating time is; conversely, the higher the cover retreating temperature, the shorter the cover retreating time. If the cover annealing temperature is lower than 100 ℃, the strength is higher, the hole expansion rate is lower and reaches more than 30 percent; if the annealing temperature is higher than 300 ℃, the strength is difficult to meet the requirement of being more than or equal to 1180 MPa. Therefore, the annealing temperature is selected to be between 100 ℃ and 300 ℃.

The invention has the beneficial effects that:

the technology provided by the invention can be used for manufacturing high-hole-expansion steel with yield strength not less than 900MPa, tensile strength not less than 1180MPa and thickness of 2-6mm, and has good elongation (transverse A)₅₀Not less than 10%), impact toughness and hole expansion performance (the hole expansion rate is not less than 30%), shows excellent matching of strength, plasticity, toughness and hole expansion performance, and has the following beneficial effects:

(1) by adopting a relatively economic component design idea and simultaneously adopting an innovative cooling and cover withdrawing process path, 1180MPa grade high-plasticity high-hole-expansion steel with excellent strength, plasticity, toughness and hole expansion performance can be obtained;

(2) the steel coil or the steel plate has excellent ultrahigh strength, plasticity and toughness matching, and simultaneously has good reaming and flanging performance, can be applied to manufacturing of parts such as automobile chassis, auxiliary frames and the like which need high-strength thinning and reaming and flanging, and has wide application prospect.

Drawings

FIG. 1 is a process flow diagram of a 1180MPa grade high plasticity high hole expansion steel manufacturing method of the present invention;

FIG. 2 is a schematic view of a rolling process in the 1180MPa grade high plasticity high hole expansion steel manufacturing method of the present invention;

FIG. 3 is a schematic view of a cooling process in the 1180MPa grade high plasticity high hole expansion steel manufacturing method of the present invention;

FIG. 4 is a schematic diagram of a cover annealing process in the 1180MPa grade high plasticity high hole expansion steel manufacturing method of the present invention;

FIG. 5 is a typical metallographic picture of a high hole expansion steel according to example 2 of the present invention;

FIG. 6 is a representative metallographic picture of a high hole expansion steel of example 4 according to the invention;

FIG. 7 is a representative metallographic picture of a high hole expansion steel according to example 6 of the present invention;

fig. 8 is a typical metallographic picture of example 8 of a high hole expansion steel according to the present invention.

Detailed Description

Referring to fig. 1 to 4, the method for manufacturing 1180MPa grade high plasticity high hole expansion steel of the present invention includes the following steps:

1) smelting and casting

Smelting by adopting a converter or an electric furnace, secondarily refining by adopting a vacuum furnace, and then casting into a casting blank or an ingot;

3) hot rolling

4) cooling down

5) annealing

6) acid pickling

The pickling speed of the strip steel can be adjusted within the range of 30-90 m/min, the pickling temperature is controlled within the range of 75-85 ℃, the withdrawal and straightening rate is controlled to be less than or equal to 1.5%, rinsing is carried out within the temperature range of 35-50 ℃, and surface drying and oiling are carried out within the temperature range of 120-140 ℃.

The components of the high hole expansion steel embodiment of the invention are shown in table 1, and tables 2 and 3 are production process parameters of the steel embodiment of the invention, wherein the thickness of a billet in a rolling process is 120 mm; table 4 shows the mechanical properties of the steel sheets of examples of the present invention.

As can be seen from Table 4, the yield strength of the steel coil is more than or equal to 900MPa, the tensile strength is more than or equal to 1180MPa, the elongation is usually between 10 and 13 percent, the impact energy is relatively stable, the impact energy at the low temperature of minus 40 ℃ is stabilized between 60 and 100J, the content of the residual austenite is changed along with different coiling temperatures, and the hole expansion ratio is more than or equal to 30 percent.

The embodiments show that the 1180MPa high-reaming steel has good matching of strength, plasticity, toughness and reaming performance, is particularly suitable for parts such as automobile chassis structures and the like which need high-strength thinning and reaming and flanging forming, such as control arms and the like, can also be used for parts such as wheels and the like which need hole flanging, and has wide application prospect.

Typical metallographic structures of steel sheets according to examples # 2, # 4, # 6 and # 8 are shown in FIGS. 5 to 8, respectively. As can be seen from the metallographic photograph, the structure is single-phase low-carbon martensite and simultaneously contains a certain amount of residual austenite, and the elongation and the hole expansibility are relatively higher under the same strength level.

Claims

1. A1180 MPa grade high plasticity high hole expansion steel comprises the following chemical components in percentage by weight: 0.06-0.10% of C, 0.8-2.0% of Si, 1.5-2.0% of Mn, less than or equal to 0.02% of P, less than or equal to 0.003% of S, 0.02-0.08% of Al, less than or equal to 0.004% of N, 0.1-0.5% of Mo, 0.01-0.05% of Ti, less than or equal to 0.0030% of O, and the balance of Fe and other inevitable impurities.

2. The 1180MPa grade high plasticity high hole expansion steel according to claim 1, further comprising one or more elements selected from the group consisting of Cr 0.5% or less, B0.002% or less, Ca 0.005% or less, Nb 0.06% or less, V0.05% or less, Cu 0.5% or less, and Ni 0.5% or less, wherein the Cr content is preferably 0.2-0.4%, and the Cu and Ni contents are preferably 0.3% or less, respectively; the content of Nb and V is preferably less than or equal to 0.03 percent respectively; the content of B is preferably 0.0005-0.0015%, and the content of Ca is preferably 0.002% or less.

3. The high plasticity high hole expansion steel of 1180MPa grade according to claim 1, wherein the C content is 0.07-0.09%.

4. The high plasticity high hole expansion steel of 1180MPa grade according to claim 1, wherein the Si content is 1.0-1.4%.

5. The high plasticity high hole expansion steel of 1180MPa grade according to claim 1, wherein the Mn content is 1.6-1.9%.

6. The high plasticity high hole expansion steel with grade 1180MPa as recited in claim 1, wherein the S content is controlled below 0.0015%.

7. The high plasticity high hole expansion steel of 1180MPa grade according to claim 1, wherein the Al content is 0.02-0.05%.

8. The high plasticity high hole expansion steel with grade 1180MPa as recited in claim 1, wherein the N content is controlled to be less than 0.003%.

9. The high plasticity high hole expansion steel of 1180MPa grade according to claim 1, wherein the Ti content is 0.01-0.03%.

10. The high plasticity high hole expansion steel with a grade of 1180MPa according to claim 1, wherein the content of Mo is 0.15-0.35%.

11. The high plasticity high pore expanding steel of 1180MPa grade according to claim 1, wherein the microstructure of the high pore expanding steel is low carbon tempered martensite.

12. The 1180MPa grade high plasticity high hole expansion steel according to claim 1 or 11, wherein the yield strength of the high hole expansion steel is not less than 900MPa, the tensile strength is not less than 1180MPa, and the elongation (in the transverse direction) is

A₅₀Not less than 10 percent) and the hole expanding rate not less than 30 percent.

13. The method for producing 1180MPa grade high plasticity high hole expansion steel according to any one of claims 1 to 12, wherein: the method comprises the following steps:

1) smelting and casting

Smelting by a converter or an electric furnace and performing secondary refining by a vacuum furnace according to the components of the alloy of claims 1-10, and then casting into a casting blank or an ingot;

3) hot rolling

4) cooling down

5) annealing

6) acid pickling

Adjusting the strip steel pickling operation speed within the range of 30-90 m/min, controlling the pickling temperature to be 75-85 ℃, controlling the withdrawal and straightening rate to be less than or equal to 1.5%, rinsing, drying the surface of the strip steel, and oiling.

14. The method as claimed in claim 13, wherein the step 6) of pickling is followed by rinsing at a temperature of 35-50 ℃, and drying and oiling the surface of the strip steel at a temperature of 120-140 ℃.