CN111041382A - 1800 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient and preparation method thereof - Google Patents

1800 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient and preparation method thereof Download PDF

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CN111041382A
CN111041382A CN201911219473.XA CN201911219473A CN111041382A CN 111041382 A CN111041382 A CN 111041382A CN 201911219473 A CN201911219473 A CN 201911219473A CN 111041382 A CN111041382 A CN 111041382A
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詹华
晋家春
王蕾
崔磊
刘永刚
李子涛
张军
谷海容
肖洋洋
彭梦都
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Maanshan Iron and Steel Co Ltd
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C21D2211/008—Martensite

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Abstract

The invention discloses 1800 MPa-grade non-coating hot forming steel with a low high-temperature friction coefficient and a preparation method thereof, wherein the 1800 MPa-grade non-coating hot forming steel comprises the following main chemical components in percentage by mass: 0.25-0.35%, Si: less than or equal to 0.5 percent, Mn: 0.5-1.5%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: less than or equal to 0.50 percent, Al: 0.01-0.06%, Ti: less than or equal to 0.04 percent, Nb + V + Mo: less than or equal to 0.5 percent, B: less than or equal to 0.003 percent, and the balance of Fe and inevitable impurities. The invention improves the surface state of the hot forming steel raw material without the coating by optimizing the components and the process, and provides a good hot forming steel raw material for the preparation of the subsequent hot forming parts.

Description

1800 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient and preparation method thereof
Technical Field
The invention belongs to the technical field of metallurgy, and relates to 1800 MPa-grade non-coating hot forming steel with a low high-temperature friction coefficient and a preparation method thereof.
Background
With the continuous development of hot forming technology, the amount of hot stamping steel is increasing. The hot forming steels widely used in the market at present are classified into products with a coating layer and products without a coating layer according to the state of the coating layer.
For a plated plate product, a protective atmosphere in a furnace is not needed in the thermal forming process, the plated layer has good high-temperature oxidation resistance in the thermal forming process, and shot blasting and oil coating treatment is not needed after thermal forming, so that the plated plate product is favored by a plurality of host factories; however, since Al — Si coated hot formed steel is limited by patents and functions depend on importation, the raw material cost is very high. At the present stage, each large host factory faces great cost pressure, so most host factories still select products without a coating, the steel products subjected to thermoforming without the coating inevitably undergo surface oxidation in the thermoforming process, the surface oxidation is not beneficial to part forming, meanwhile, the existence of oxide skin seriously abrades a grinding tool, and shot blasting treatment is needed after thermoforming; therefore, for non-plated hot-formed steel products, how to reduce surface oxidation, improve the service life of the die, and reduce the high-temperature friction coefficient becomes the main direction of research on non-plated hot-formed steel.
On the other hand, the hot forming steel widely used in the market at present is 1500MPa strength level, and with the stricter laws and regulations on energy consumption and safety performance of automobiles, and the research on lightweight of automobiles, people are going to be deep, and hot forming steel with higher strength level becomes a research hotspot.
Not only is high strength required for hot formed parts under complex load conditions, but good ductility and toughness is also required. However, since all the steel obtained after hot forming and quenching is a martensite structure, the strength is very high, but the toughness is insufficient, the strength is 1800MPa or more, the elongation is only about 4%, and the three-point bending angle is generally 50 degrees or less.
It is found through search that patent CN201811050163.5 hot-formed steel plate and method for improving elongation of hot-formed steel plate have main chemical components (wt%): c: 0.18 to 0.23%, Si: 0.10 to 0.25%, Mn: 1.0-1.3%, P: less than or equal to 0.015 percent, S: less than or equal to 0.01 percent, Ti: 0.01-0.05%, B: 0.001-0.0035%, Cr: 0.1-0.3%, La: 0.0015-0.0025%, and the balance of Fe and inevitable impurities. In the preparation process of raw materials, a high-elongation steel plate is obtained mainly by adding rare earth La into the steel, optimizing rolling and slow cooling treatment processes, and the elongation of the hot-rolled steel plate reaches 25%; on the other hand, by adding the rare earth La, the purity of the steel can be improved, the starting temperature and the ending temperature of martensite transformation are changed, the residual austenite number is reduced, the fine structure of martensite is obtained, and the microstructure appearance of the steel is changed. However, this method is only applicable to hot rolled products, and for hot press formed materials, increasing the elongation of the raw material does not represent that the elongation after quenching can be improved to some extent.
Patent CN201480063861.2 hot-formed steel sheet member, its manufacturing method and hot-formed steel sheet, the main chemical components (wt%) of the steel are: c: 0.100-0.340%, Si: 0.50 to 2.00%, Mn: 1.00-3.00%, P: less than or equal to 0.05 percent, S: less than or equal to 0.01 percent, Als: 0.001 to 1.000%, N: less than or equal to 0.0100 percent and the balance of Fe and inevitable impurities. The structure (area%) of the steel is ferrite: 5% -50%, martensite and bainite: 45-90% in total, ferrite + martensite + bainite: the total is more than 90%. The elongation after thermoforming is more than or equal to 12 percent, and the bending angle of the V-bend test is more than 90 degrees.
Patent CN201110259342.1 is a method for preparing a dual-phase hot forming steel, the main chemical components (wt%) of the steel are: c: 0.1-0.5%, Si: 0.3 to 2.5%, Mn: 1.0-3.0%, P: less than or equal to 0.02 percent, S: less than or equal to 0.01 percent, Al: 1.0-3.0%, N: less than or equal to 0.01 percent, and the balance of Fe and inevitable impurities. The production process comprises the following steps: smelting → hot rolling → hot forming, the invention adopts Al micro alloying treatment, compared with the traditional hot forming steel, the invention has the advantages that: the hot forming heating temperature is low, and the surface oxidation is reduced; the hot formed structure is a ferrite + martensite dual-phase structure.
In summary, currently, regarding the preparation of hot forming steel raw materials, optimization is mainly performed from the viewpoint of improving material performance, and the main approach is component and process improvement. The method has no improvement effect on the problems that the oxide scale is generated in the hot forming process of the non-coating hot forming steel, the forming performance is poor, and parts with complex structures cannot be generated.
In addition, as for hot forming steel with strength of more than or equal to 1800MPa, a search shows that patent CN 106811689B is a preparation method of hot forming steel with tensile strength of more than or equal to 2000MPa, and the steel comprises the following components in percentage by mass: 0.3-0.5%, Si: 1.2-1.7%, Mn: 1.4-2.0%, B: 0.001-0.01%, Ti: 0.05-0.1%, P: less than or equal to 0.008 percent, S: less than or equal to 0.005 percent, Cr: 0.6-1.2%, Al: 0.01 to 0.07%, Nb: 0.01-0.08%, and the balance of Fe and inevitable impurity elements. The strength is improved mainly by adding 0.3-0.5% of C, 1.2-1.7% of Si, 1.4-2.0% of Mn, the hardenability is improved by adding 0.6-1.2% of Cr and 0.001-0.01% of B, and the elongation is improved by adding 0.01-0.08% of Nb; in addition, the strength of the raw material is reduced through the cover annealing, and the shearing processing before the hot forming is facilitated. However, the addition of 1.4-2.0% of Mn in the invention is easy to generate a banded structure, and is not favorable for the cold bending performance of the formed part; 1.2 to 1.7 percent of Si is added, which is unfavorable for the surface quality control in the actual hot rolling and cold rolling production processes; and 0.6-1.2% of Cr is added, so that the risk of casting blank cracking in the continuous casting production process is increased.
Patent CN 106811681B is a method for preparing B-free hot forming steel, wherein the steel comprises the following components in percentage by mass: 0.25-0.5%, Si: 0.7-1.2%, Mn: 0.5-1.3%, Al: 0.01-0.08%, P: less than or equal to 0.015 percent, S: less than or equal to 0.008 percent, Cr: 1.0-3.0%, Ti: 0.02 to 0.09%, Mo: 0.05 to 0.25%, Nb: 0.02-0.09%, and the balance of Fe and inevitable impurity elements. The production process of the invention comprises the following steps of heating at 1200 ℃, keeping the temperature for 1h, and finishing rolling: 870 ℃, coiling temperature: 660 ℃, then heating to 900 ℃, preserving heat for 3min, then rapidly cooling to 260 ℃, and then air-cooling to room temperature to obtain a complete martensite structure. Although the material obtained by the invention has low cost, the addition of 0.7-1.2% of Si is unfavorable for the surface quality control in the actual hot rolling and cold rolling production processes; 1.0-3.0% of Cr is added, so that the risk of casting blank cracking in the continuous casting production process is increased; and 0.02-0.09% of Ti is added, large-particle TiN can be separated out in the actual production process, stress concentration points are easy to form during application, and the collision performance of parts is not favorable; on the other hand, the 660 ℃ coiling is adopted, the band-shaped structure in the finished product material is obvious, the cold bending performance of the part is not good, and the precipitate of Nb which is not good in high-temperature coiling is fully dispersed and precipitated, so that the effect of refining grains in the hot forming process is not good.
The patent CN 106119693A uses the thin slab to roll the thin hot forming steel with the tensile strength more than or equal to 2100MPa directly and the production method, the component mass percentage of the steel is C: 0.41-0.50%, Si: 0.45-0.65%, Mn: 1.6-2.0%, B: 0.004-0.005%, P: less than or equal to 0.006 percent, S: less than or equal to 0.004%, Cr: 0.50-0.65%, Als: 0.015 to 0.060%, Ti: 0.046-0.060% or Nb: 0.046-0.060%, Mo: 0.36-0.60%, Ni: 0.21-0.35%, N: less than or equal to 0.004 percent, and the balance of Fe and inevitable impurity elements. The preparation method comprises the following steps: smelting in an electric furnace or a converter, refining, continuous casting, wherein the heating temperature is 1230-1250 ℃, the finish rolling temperature is 880-920 ℃, and the coiling temperature is 585-615 ℃. The yield strength of the prepared material is more than or equal to 1450MPa, the tensile strength is more than or equal to 2100MPa, and the elongation rate A is higher than80The invention is mainly used for preparing hot forming steel materials in a short process, and has the advantage of low cost compared with the traditional steel making, hot rolling, cold rolling and annealing process. However, the addition of 0.41-0.50% of C in the patent increases the hardness of quenched martensite, but is actually not beneficial to the ductility and toughness of the formed part; 1.6-2.0% of Mn is added, so that a banded structure is easily generated, and the cold bending property of the formed part is not favorable; moreover, 0.21-0.35% of Ni is added, so that the alloy cost of the product is increased; and the hot-rolled finished product raw material has a decarburized layer, and the decarburized layer is further aggravated after hot forming, so that the profile size and the surface quality of the manufactured part after shot blasting are influenced.
Disclosure of Invention
In order to solve the problems, the invention provides 1800 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient and a preparation method thereof, which improve the surface state of the non-coating hot forming steel raw material through component and process optimization and provide a good hot forming steel raw material for the preparation of subsequent hot forming parts.
The 1800 MPa-grade uncoated hot forming steel with the low high-temperature friction coefficient comprises the following main chemical components in percentage by mass: 0.25-0.35%, Si: less than or equal to 0.5 percent, Mn: 0.5-1.5%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: less than or equal to 0.50 percent, Al: 0.01-0.06%, Ti: less than or equal to 0.04 percent, Nb + V + Mo: less than or equal to 0.5 percent, B: less than or equal to 0.003 percent, and the balance of Fe and inevitable impurities.
Further, the 1800 MPa-grade non-coating hot forming steel comprises the following main chemical components in percentage by mass: 0.28-0.35%, Si: less than or equal to 0.1 percent, Mn: 0.8-1.2%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.26-0.50%, Al: 0.01-0.06%, Ti: less than or equal to 0.01 percent, Nb + V + Mo: less than or equal to 0.5 percent, and the balance of Fe and inevitable impurities.
1) Chemical components of a matrix:
c: 0.25 to 0.35%, and preferably 0.28 to 0.35% for 1800MPa grade hot formed steel, since C is one of the main elements that increases the martensitic strength.
Si: not more than 0.5%, preferably not more than 0.1%, and addition of Si element which easily generates Fe (Si) in the heating process in the hot rolling productionxOy) Namely 'fayalite', has strong adhesion, is adhered to the surface of a steel plate and is not easy to clean, and the surface quality of the steel plate is influenced.
Mn: 0.5-1.5%, preferably 0.8-1.2% for 1800MPa grade hot forming steel, and the main reason for reducing the Mn content is that the coiling temperature cannot be too low during hot rolling, otherwise bainite or a small amount of martensite structure can be generated, thereby improving the hot coil strength and further increasing the difficulty of the acid rolling process; on the other hand, when the coiling temperature is 600 ℃ or higher, band-shaped structure defects are easily generated in the hot-rolled structure, and the generation of the band-shaped structure is difficult to eliminate in the subsequent cold rolling and annealing processes, so that the addition of Mn content needs to be reduced in order to reduce the band-shaped structure defects and make the final structure uniform.
P：≤0.020％。
S：≤0.010％。
Cr: not more than 0.50%, preferably 0.26-0.50% for 1800MPa grade hot formed steel, Cr is an element for improving hardenability, and the hardenability of steel grade is increased by coordination addition.
Al：0.01-0.06％。
Ti: not more than 0.04%, preferably not more than 0.01% for 1800MPa grade hot formed steel, because sufficient hardenability of steel grade is ensured by adding alloy elements such as C, Mn, Cr, Mo, etc., therefore, B does not need to be added to improve hardenability, and further addition of Ti element can be eliminated.
Nb + V + Mo: the steel is characterized in that the steel is equal to or less than 0.5%, one to three micro-alloy elements of Nb, V and Mo can be selectively added to 1800 MPa-grade hot forming steel, the three elements of Nb, V and Mo are preferably added, the total addition amount is equal to or less than 0.5%, the Nb and V are added mainly for precipitating dispersed and distributed fine precipitates in the rolling, annealing and heat treatment processes, on one hand, grains are refined, the toughness is improved, on the other hand, hydrogen traps are formed, the delayed cracking resistance is improved, the Mo element is added mainly for further refining the grains, carbides are respectively more uniform, the hardenability of the steel is further improved, the addition of B and Ti elements is reduced, the possibility of precipitation of large-grain TiN is eliminated, and the matrix structure uniformity of the steel is improved.
B: not more than 0.003%, and preferably not added to 1800MPa grade hot forming steel, because sufficient hardenability of steel grade is ensured by adding alloy elements such as C, Mn, Cr, Mo, etc., therefore, B does not need to be added to improve hardenability.
The balance of Fe and inevitable impurities.
A preparation method of 1800 MPa-level plating-free hot forming steel with low and high-temperature friction coefficients adopts the process flows of steel making → casting blank → hot rolling → acid pickling and cold rolling → annealing → blanking → hot forming and the like, and comprises the following specific steps:
1) production of steel
For 1800 MPa-grade hot forming steel, high-carbon protective slag is preferentially selected due to the difference of components;
2) continuous casting and hot rolling production
Tapping temperature: reducing the steel burning temperature at 1000-1230 ℃, and reducing decarburization of a casting blank during heating;
controlling the atmosphere in the heating furnace: the air-fuel ratio of the weak reducing atmosphere is 1.0-1.05;
finish rolling is carried out by adopting a CVC rolling mill, and an edge heater is started;
the finishing temperature is as follows: 850-900 ℃;
laminar cooling: adopting front-section cooling and adopting side-spraying treatment in a laminar cooling section;
coiling temperature: for 1800MPa grade hot forming steel, the coiling temperature is less than or equal to 700 ℃;
coiling tension: for a steel coil with the thickness of 3.0-6.0 mm, the coiling tension is more than or equal to 35 MPa; for a steel coil with the thickness of 2.0-3.0 mm, the coiling tension is more than or equal to 45 MPa;
3) acid pickling
Removing iron scales generated in the hot rolling process;
4) cold rolling
The cold rolling reduction is more than or equal to 50 percent;
5) annealing process control
For the steel coil with the thickness of 1.6-2.5 mm produced by continuous annealing, in the annealing process section, the annealing temperature is 780-820 ℃, the annealing time is 4-8 min, and the dew point in the furnace is controlled to be less than or equal to minus 30 ℃;
for the steel coil with the thickness less than 1.6mm produced by continuous annealing, in the annealing process section, the annealing temperature is 750-800 ℃, the annealing time is 6-12 min, and the dew point in the furnace is controlled to be less than or equal to-30 ℃;
for the product produced by the cover annealing process, the cold point temperature is 620 ℃ plus or minus 20 ℃, the soaking temperature is 710 ℃ plus or minus 20 ℃, the heating section is less than 18h, the soaking section time is 10 h-15 h, and the hydrogen purging is set as follows: when the temperature in the furnace is less than or equal to 600 ℃, the purging amount is more than 15m3/h, and when the temperature in the furnace is more than 600 ℃, the hydrogen purging amount is less than or equal to 10-15 m3/h, so that the surface of the strip steel is ensured to be clean and free of carbide or oxidation color;
6) edge cutting process
The double trimming amount of the finished product is 25-50 mm;
7) flattening process
The leveling roller adopts a low-roughness roller surface, and the roughness Ra of the roller surface is less than or equal to 0.8 mu m;
8) thermoforming process
Heating temperature: 800 ℃ and 1000 ℃;
controlling the atmosphere in the furnace: the furnace is protected by introducing N2, the pressure of N2 is more than 1Pa, the proportion of N2 is more than 99.9 percent, and the dew point in the furnace is less than or equal to minus 45 ℃;
heating time: 2-6 min;
transfer time: < 10 s;
pressure maintaining time: 10s-20 s;
cooling rate: the temperature is more than or equal to 25 ℃/s, and the matrix structure is a complete martensite structure after the part is formed;
10) after the part is taken out of the die, the part is subjected to laser cutting treatment and shot blasting and oil coating treatment.
Further, in the step 2), the coiling temperature is 600-700 ℃.
Further, in the step 7), the roughness Ra of the roller surface is less than or equal to 0.6 μm.
Further, in the step 8), the heating temperature is 850-930 ℃.
Further, in the step 8), the dwell time is 15 s.
Compared with the prior Chinese patent CN 106811689B, the high-toughness hot forming steel with uniform structure and tensile strength of more than or equal to 1800MPa is obtained by adopting the component design of low Si, low Mn, low Cr, no Ti, no B and Mo addition and combining the low-temperature coiling and continuous annealing process, and the production efficiency is improved.
Compared with the prior Chinese patent CN 106811681B, the high-toughness hot forming steel with the tensile strength of more than or equal to 1800MPa is obtained by adopting the low-Si, low-Cr and Ti-free component design and combining the low-temperature coiling and continuous annealing process, and the high-toughness hot forming steel has no banded structure and improves the production efficiency.
Compared with the prior Chinese patent CN 106119693A, the component design of the invention does not contain elements such as noble metal Ni, and the like, so the alloy cost is lower, and the steelmaking continuous casting process is easier to control; meanwhile, the negative problems of raw material surface decarburization and the like do not exist, and the molded surface size and the surface quality of the hot forming part are favorably ensured.
The tensile strength of the hot forming part obtained by the method is more than or equal to 1800MPa, the three-point bending angle is more than or equal to 50 degrees, and the cold bending performance reaches the cold bending performance level of 1500MPa hot forming steel commonly used in the market at present, so that the method improves the strength and ensures higher cold bending performance, and provides a raw material with better light weight effect and safety performance when the body of a main engine plant is designed and selected.
The invention has the following beneficial effects:
1) the oil storage amount on the surface of the strip steel is reduced due to the reduction of the surface roughness, and the pollution on the surface of the steel plate is reduced due to the small amount of oil on the surface in the heating process, so that the hot forming stamping environment can be improved;
2) the reduction of the surface roughness reduces the high-temperature friction in the hot stamping forming process, thereby prolonging the service life of the grinding tool;
3) the reduction of the surface roughness reduces the high-temperature friction between the material and the die in the hot stamping forming process, thereby reducing the thinning rate of the deep-drawn part and improving the high-temperature forming performance of the part; meanwhile, the part can be well jointed with the die, so that the hardenability is improved;
4) the hot forming raw material prepared according to the components and the process does not contain Ti, so that the alloy cost is saved, large-particle TiN is prevented from being separated out, and the cold bending performance of a finished product is improved; the components of the finished product are uniformly distributed by adopting the low Mn and Mo component design, so that the risk of banded structures is reduced; NbV alloy elements are added, so that the matrix structure is uniformly refined, and precipitates of a finished product are uniformly dispersed and distributed; after hot forming, the yield strength of the part is 1264MPa, the tensile strength is 1895MPa, the elongation is 5.6%, and the cold bending angle of the hot formed part can reach 51 degrees.
Drawings
FIG. 1 shows a base structure of a raw material under an optical microscope at a magnification of 100;
FIG. 2 shows the matrix structure of the raw material under an optical microscope at 500 times;
FIG. 3 is prior austenite grain size after hot forming;
FIG. 4 is a martensitic structure after hot forming;
FIGS. 5 and 6 show the surface morphology of the strip steel under the condition that the surface roughness Ra is 2.0 μm;
FIGS. 7 and 8 show the surface morphology of the strip steel under the condition that the surface roughness Ra is 0.8 μm;
FIGS. 9 and 10 show the surface morphology of the strip steel under the condition that the surface roughness Ra is 0.3 μm;
FIG. 11 shows the high temperature friction coefficient of the steel strip under the condition that the surface roughness Ra is 2.0 μm;
FIG. 12 shows the high temperature friction coefficient of the steel strip under the condition that the surface roughness Ra is 0.8 μm;
FIG. 13 shows the high temperature friction coefficient of the steel strip under the condition that the surface roughness Ra is 0.3 μm;
FIG. 14 shows a thick oxide layer (N) on the surface of a part with a surface roughness Ra of 2.0 μm2Gas protection);
FIG. 15 shows that the oxide layer on the surface of the part was almost eliminated (N) under the condition that the surface roughness Ra was 0.3 μm2Gas protection);
FIG. 16 shows that the surface roughness Ra of the part was 0.8 μm, but there was no significant oxidation layer on the surface of the part, but slight carbonization of the rust preventive oil was present.
Detailed Description
In order to further illustrate the present invention, the following detailed description of the invention is given with reference to the examples and the accompanying figures 1-16.
The 1800 MPa-grade uncoated hot forming steel with the low high-temperature friction coefficient comprises the following main chemical components in percentage by mass: 0.25-0.35%, Si: less than or equal to 0.5 percent, Mn: 0.5-1.5%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: less than or equal to 0.50 percent, Al: 0.01-0.06%, Ti: less than or equal to 0.04 percent, Nb + V + Mo: less than or equal to 0.5 percent, B: less than or equal to 0.003 percent, and the balance of Fe and inevitable impurities.
Preferably, the 1800 MPa-grade non-coating hot forming steel comprises the following main chemical components in percentage by mass: 0.28-0.35%, Si: less than or equal to 0.1 percent, Mn: 0.8-1.2%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.26-0.50%, Al: 0.01-0.06%, Ti: 0.01% or less (preferably Ti may not be added), Nb + V + Mo: less than or equal to 0.5 percent, and the balance of Fe and inevitable impurities.
The steel plates of the following three groups of examples have the same chemical composition, and the values in the examples are selected to meet the numerical specification of the invention.
As shown in table 1:
table 1 Steel plate chemical composition, wt.%
Examples C Si Mn P S Al Cr Ti B Nb V Mo
1800MPa 0.30 0.21 1.00 0.01 0.002 0.039 0.200 0.002 0.001 0.030 0.031 0.15
Three groups of materials of the same composition were produced according to the manufacturing method of the present invention, with only one parameter of surface roughness changed, as shown in table 2.
Three groups of materials of the same composition were produced according to the manufacturing method of the present invention, with only one parameter of surface roughness changed, as shown in table 2.
A preparation method of 1800 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient comprises the following steps:
1) production of steel
Based on the function of the covering slag in the steelmaking process (1, isolating molten steel from air; 2, playing a lubricating role in the continuous casting process), the high-carbon covering slag is preferentially selected for the 1800 MPa-grade hot forming steel due to the difference of components.
2) Continuous casting and hot rolling production
The casting blank is preferably subjected to tissue production in a hot charging mode, so that the production rhythm is improved, and the risk of casting blank cracks is reduced; if the structure production can not be carried out by adopting a hot charging mode, the casting blank obtained after continuous casting needs to enter a heat preservation pit for slow cooling treatment, and the slow cooling treatment has two purposes, namely reducing the risk of cracks, and on the other hand, reducing the hydrogen content in the casting blank by slow cooling and hydrogen diffusion.
Tapping temperature: reducing the steel burning temperature at 1000-1230 ℃, and reducing decarburization of a casting blank during heating;
controlling the atmosphere in the heating furnace: the air-fuel ratio of the weak reducing atmosphere is 1.0-1.05.
And (3) rolling by adopting a CVC rolling mill in finish rolling, and opening an edge heater to eliminate uneven organization performance in the direction vertical to the strip steel caused by too fast cooling of the edge.
The finishing temperature is as follows: 850-900 ℃;
laminar cooling: front section cooling is adopted, so that the phase change of the strip steel is finished before the strip steel enters a coiler, and the risk of coil collapse is eliminated; side spraying (gas) treatment is adopted in the laminar cooling section, so that laminar cooling accumulated water on the upper surface of the strip steel is eliminated, and the upper surface and the lower surface of the strip steel are uniformly cooled;
coiling temperature: for 1800 MPa-grade hot forming steel, the coiling temperature is less than or equal to 700 ℃, 600-700 ℃ is preferred, the risk of hot rolling strip-shaped structures is reduced due to the reduction of Mn content in the previous component design, and the reason that low-temperature coiling is not selected is as follows: the addition of high alloy element content increases hardenability, and if low-temperature coiling is adopted, the proportion of hard phases is increased, the strength of a hot-rolled coil is increased, and difficulty is brought to a subsequent acid rolling process, so that low-temperature coiling is not adopted when the coiling temperature is selected.
Coiling tension: for a steel coil with the thickness of 3.0-6.0 mm, the coiling tension is more than or equal to 35 MPa; for a steel coil with the thickness of 2.0-3.0 mm, the coiling tension is more than or equal to 45 MPa; so as to ensure the rolling up of the hot-rolled coil and reduce the risk of coil collapse.
3) Acid pickling
And removing the iron scale generated in the hot rolling process.
4) Cold rolling
The cold rolling reduction is more than or equal to 50 percent, the enough refinement of crystal grains is ensured, the smaller the crystal grains are, the more sufficient the subsequent recovery recrystallization process is, the better the structure uniformity is, and therefore, the better the cold bending performance after forming is.
5) Annealing process control
For the steel coil with the thickness of 1.6-2.5 mm produced by continuous annealing, in the annealing process section, the annealing temperature is 780-820 ℃, the annealing time is 4-8 min, and the dew point in the furnace is controlled to be less than or equal to minus 30 ℃. For the steel coil with the thickness less than 1.6mm produced by continuous annealing, in the annealing process section, the annealing temperature is 750-800 ℃, the annealing time is 6-12 min, and the dew point in the furnace is controlled to be less than or equal to-30 ℃.
The main purpose of annealing according to the annealing temperature and the annealing time is to ensure that the matrix is subjected to uniform annealing and further eliminate the banded structure.
For the product produced by the cover annealing process, the cold point temperature is 620 ℃ plus or minus 20 ℃, the soaking temperature is 710 ℃ plus or minus 20 ℃, the heating section is less than 18h, the soaking section time is 10 h-15 h, and the hydrogen purging is set as follows: when the temperature in the furnace is less than or equal to 600 ℃, the purging amount is more than 15m3/h, and when the temperature in the furnace is more than 600 ℃, the hydrogen purging amount is less than or equal to 10-15 m3/h, so that the surface of the strip steel is ensured to be clean and free of carbide or oxidation color.
6) Edge cutting process
The double trimming amount of the finished product is 25-50 mm, and the insufficient thickness area and the uneven tissue performance part of the hot coil caused by the reduced thickness of the edge part or the high cooling rate of the edge part are completely cut off.
7) Flattening process
The leveling roller adopts a low-roughness roller surface, the roughness Ra of the roller surface is less than or equal to 0.8 mu m, and the Ra is preferably less than or equal to 0.6 mu m, otherwise, the effect of improving the high-temperature friction performance cannot be achieved in the hot forming process.
8) Thermoforming process
Heating temperature: 800 ℃ and 1000 ℃, and the heating temperature is preferably 850-930 ℃. The heating temperature cannot be less than 850 ℃, otherwise, the matrix structure cannot be completely austenitized in the heating process, so that the martensite structure cannot be obtained in the quenching process, and the strength of the formed part cannot be ensured; the heating temperature cannot be more than 930 ℃, otherwise, coarse austenite grains are formed, and the cold bending performance after hot forming is reduced.
Controlling the atmosphere in the furnace: the furnace is protected by introducing N2, the pressure of N2 is more than 1Pa, the proportion of N2 is more than 99.9 percent, and the dew point in the furnace is less than or equal to minus 45 ℃, thereby ensuring that the atmosphere in the furnace has no oxidizing or reducing atmosphere.
Heating time: 2-6min, combining the heating temperature range, the heating time cannot be less than 2min, otherwise, complete austenitizing cannot be realized; the heating time cannot be more than 6min, otherwise, austenite grains become coarse, and the cold bending performance of the finished part is affected.
Transfer time: when the transfer time is less than 10s, the microstructure transformation of ferrite, pearlite and the like can occur after the transfer time exceeds 10s, so that the martensite content in the final part microstructure is insufficient, the mechanical property requirement can not be met, and the transfer time is more than 10s, so that the production rhythm can be influenced.
The dwell time is more than or equal to 10s, preferably 15s, on the basis of the process, the dwell time is not suitable to be less than 10s, otherwise, the temperature of the part taken out of a mold is high, the part is cooled and deformed when being cooled in air, the dwell time is not suitable to be more than 20s, and otherwise, the production rhythm is influenced.
Cooling rate: the temperature is more than or equal to 25 ℃/s, and the matrix structure is a complete martensite structure after the part is formed.
9) After the part is taken out of the die, the part is subjected to laser cutting treatment and shot blasting and oil coating treatment.
TABLE 2 relationship between surface roughness of raw material and high temperature coefficient of friction
Examples Surface roughness Ra mum Coefficient of friction at high temperature
1 2.0 0.76
2 0.8 0.64
3 0.3 0.60
Table 3 shows the properties after thermoforming
TABLE 3 post-thermoforming Properties
Examples Yield strength Mpa Tensile strength Mpa Elongation percentage% Cold bending property °
2 1264 1895 5.6 57.0
3 1301 1868 5.5 56.5
Example 1
In this example, the surface roughness Ra was 2.0 μm and the high-temperature friction coefficient averaged 0.76.
The surface appearance of the strip steel is shown in fig. 5 and fig. 6, and the high-temperature friction coefficient of the strip steel is shown in fig. 11.
As shown in fig. 14, the part has a thicker oxide layer on its surface.
Example 2
In this example, the surface roughness Ra was 0.8 μm and the high-temperature friction coefficient average was 0.64.
The surface appearance of the strip steel is shown in fig. 7 and fig. 8, and the high-temperature friction coefficient of the strip steel is shown in fig. 12.
As shown in FIG. 16, there was no significant oxide layer on the surface of the part, but slight carbonization of the rust preventive oil was present.
Example 3
In this example, the surface roughness Ra was 0.3 μm and the high-temperature friction coefficient average value was 0.60.
The surface appearance of the strip steel is shown in FIG. 9 and FIG. 10, and the high-temperature friction coefficient of the strip steel is shown in FIG. 13.
As shown in fig. 15, the oxide layer on the surface of the part is almost eliminated.
As can be seen from FIGS. 14, 15 and 16, the oxide, rust preventive oil carbonized contamination of the surface of the parts was reduced as the surface roughness of the raw material was reduced.
As can be seen from fig. 11, 12 and 13, the friction coefficient of the uncoated hot formed steel product at high temperature decreases with the decrease of the original surface roughness of the strip.
The above embodiments have been described in detail to illustrate the object and practice of the invention, it should be understood that the above embodiments are only specific embodiments of the invention, and the invention is not limited by the above embodiments, and various modifications, equivalent substitutions, improvements and the like within the spirit and principle of the invention or by using the technical concept and technical scheme of the invention are within the protection scope of the invention.

Claims (8)

1. The 1800 MPa-grade non-coating hot forming steel with the low high-temperature friction coefficient is characterized by comprising the following main chemical components in percentage by mass: 0.25-0.35%, Si: less than or equal to 0.5 percent, Mn: 0.5-1.5%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: less than or equal to 0.50 percent, Al: 0.01-0.06%, Ti: less than or equal to 0.04 percent, Nb + V + Mo: less than or equal to 0.5 percent, B: less than or equal to 0.003 percent, and the balance of Fe and inevitable impurities.
2. The 1800MPa grade uncoated hot forming steel with low high-temperature friction coefficient as claimed in claim 1, wherein the 1800MPa grade uncoated hot forming steel comprises the following main chemical components in percentage by mass: 0.28-0.35%, Si: less than or equal to 0.1 percent, Mn: 0.8-1.2%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.26-0.50%, Al: 0.01-0.06%, Ti: less than or equal to 0.01 percent, Nb + V + Mo: less than or equal to 0.5 percent, and the balance of Fe and inevitable impurities.
3. The 1800MPa grade uncoated hot formed steel with low high temperature coefficient of friction of claim 2, wherein the Ti element is not added.
4. A method for preparing 1800MPa grade uncoated hot formed steel with low high temperature friction coefficient according to any of claims 1-3, characterized by the specific steps of:
1) production of steel
For 1800 MPa-grade hot forming steel, high-carbon protective slag is preferentially selected due to the difference of components;
2) continuous casting and hot rolling production
Tapping temperature: reducing the steel burning temperature at 1000-1230 ℃, and reducing decarburization of a casting blank during heating;
controlling the atmosphere in the heating furnace: the air-fuel ratio of the weak reducing atmosphere is 1.0-1.05;
finish rolling is carried out by adopting a CVC rolling mill, and an edge heater is started;
the finishing temperature is as follows: 850-900 ℃;
laminar cooling: adopting front-section cooling and adopting side-spraying treatment in a laminar cooling section;
coiling temperature: for 1800MPa grade hot forming steel, the coiling temperature is less than or equal to 700 ℃;
coiling tension: for a steel coil with the thickness of 3.0-6.0 mm, the coiling tension is more than or equal to 35 MPa; for a steel coil with the thickness of 2.0-3.0 mm, the coiling tension is more than or equal to 45 MPa;
3) acid pickling
Removing iron scales generated in the hot rolling process;
4) cold rolling
The cold rolling reduction is more than or equal to 50 percent;
5) annealing process control
For the steel coil with the thickness of 1.6-2.5 mm produced by continuous annealing, in the annealing process section, the annealing temperature is 780-820 ℃, the annealing time is 4-8 min, and the dew point in the furnace is controlled to be less than or equal to minus 30 ℃;
for the steel coil with the thickness less than 1.6mm produced by continuous annealing, in the annealing process section, the annealing temperature is 750-800 ℃, the annealing time is 6-12 min, and the dew point in the furnace is controlled to be less than or equal to-30 ℃;
for the product produced by the cover annealing process, the cold point temperature is 620 ℃ plus or minus 20 ℃, the soaking temperature is 710 ℃ plus or minus 20 ℃, the heating section is less than 18h, the soaking section time is 10 h-15 h, and the hydrogen purging is set as follows: when the temperature in the furnace is less than or equal to 600 ℃, the purging amount is more than 15m3/h, and when the temperature in the furnace is more than 600 ℃, the hydrogen purging amount is less than or equal to 10-15 m3/h, so that the surface of the strip steel is ensured to be clean and free of carbide or oxidation color;
6) edge cutting process
The double trimming amount of the finished product is 25-50 mm;
7) flattening process
The leveling roller adopts a low-roughness roller surface, and the roughness Ra of the roller surface is less than or equal to 0.8 mu m;
8) thermoforming process
Heating temperature: 800 ℃ and 1000 ℃;
controlling the atmosphere in the furnace: the furnace is protected by introducing N2, the pressure of N2 is more than 1Pa, the proportion of N2 is more than 99.9 percent, and the dew point in the furnace is less than or equal to minus 45 ℃;
heating time: 2-6 min;
transfer time: < 10 s;
pressure maintaining time: 10s-20 s;
cooling rate: the temperature is more than or equal to 25 ℃/s, and the matrix structure is a complete martensite structure after the part is formed;
9) after the part is taken out of the die, the part is subjected to laser cutting treatment and shot blasting and oil coating treatment.
5. The method for preparing 1800MPa grade uncoated hot formed steel with low high temperature friction coefficient according to claim 3, wherein the coiling temperature in the step 2) is 600-700 ℃.
6. The method as claimed in claim 3, wherein the roll surface roughness Ra of step 7) is less than or equal to 0.6 μm.
7. The method for preparing 1800MPa grade non-coating hot forming steel with low high temperature friction coefficient according to claim 3, wherein, in the step 8), the heating temperature is 850-930 ℃.
8. The method of claim 3, wherein the dwell time in step 8) is 15 s.
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CN112570868B (en) * 2020-12-11 2022-08-16 马鞍山钢铁股份有限公司 Method for improving corrosion resistance of resistance spot welding spot of 1800 MPa-grade hot forming steel
CN112570868A (en) * 2020-12-11 2021-03-30 马鞍山钢铁股份有限公司 Method for improving corrosion resistance of resistance spot welding spot of 1800 MPa-grade hot forming steel
CN113265513A (en) * 2021-05-21 2021-08-17 新疆八一钢铁股份有限公司 Annealing process for eliminating banded structure of 25 steel cold-rolled sheet
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CN113957349A (en) * 2021-10-26 2022-01-21 江苏沙钢集团有限公司 600 MPa-grade hot forming steel and production method thereof
CN113957350A (en) * 2021-10-26 2022-01-21 江苏沙钢集团有限公司 2000 MPa-grade hot forming steel and production method thereof
CN113913700A (en) * 2021-10-26 2022-01-11 江苏沙钢集团有限公司 1700 MPa-grade hot forming steel and production method thereof
CN113913700B (en) * 2021-10-26 2023-01-24 江苏沙钢集团有限公司 1700 MPa-grade hot forming steel and production method thereof
CN113957349B (en) * 2021-10-26 2022-09-06 江苏沙钢集团有限公司 600 MPa-grade hot forming steel and production method thereof
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CN114292996A (en) * 2021-11-26 2022-04-08 铃木加普腾钢丝（苏州）有限公司 Process for heat treatment of steel wire oxidation layer
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CN114657456A (en) * 2022-02-15 2022-06-24 鞍钢集团北京研究院有限公司 1800 MPa-grade high-toughness hot forming steel and heat treatment process thereof
CN115572897A (en) * 2022-09-19 2023-01-06 邯郸钢铁集团有限责任公司 1500 MPa-grade commercial automobile box steel plate and manufacturing method thereof
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Application publication date: 20200421