Patent Application
20250019812
The present disclosure relates to a hot-rolled steel sheet and a method for manufacturing the same.
A high-strength hot-rolled steel sheet may be applied in various uses, including a boom arm for a special purpose vehicle such as a crane, a concrete pumping truck, and the like, a truck, and a frame of a trailer. A thickness of the steel sheet used for this purpose is generally about 3 to 10 mm, and a high-strength hot-rolled steel sheet, which is thicker than a general steel sheet for automobiles requires not only high yield strength to support a design load, but also excellent shape quality for part processing and stability. In particular, when the shape quality of the high-strength hot-rolled steel sheet is excellent, the quality remains sound even after being processed, which has the advantage of increasing the stability of large structures.
Patent Document 1 is a technology which is intended to secure the shape quality by minimizing residual stress by controlling alloy composition and annealing and cooling conditions. Patent Document 2 is a technology which is intended to secure the shape quality by controlling the alloy composition and annealing and cooling conditions and simultaneously, further performing a heat-treatment process.
However, the Patent Documents 1 and 2 disclose an annealing process that can apply various cooling conditions as a method for manufacturing a cold-rolled steel sheet, but in the case of a hot-rolled steel sheet, unlike the cold-rolled steel sheet, the hot-rolled steel sheet is manufactured without additional processes after hot rolling, so that due to rapid phase transformation and high yield strength during cooling, the shape quality of the steel sheet may deteriorate significantly even after shape correction. In addition, in the case of a general high-strength hot-rolled steel sheet, the hot-rolled steel sheet may be manufactured to obtain actual target physical properties, but in the case of a high-strength hot-rolled steel sheet with a yield strength of 900 MPa or more, it is actually difficult to improve the shape quality through shape correction which is commonly used.
Accordingly, there is a demand for the development of technology that can increase shape correction properties for the high-strength hot-rolled steel sheet with high yield strength.
(Patent Document 1) Korean Patent Publication No. 10-1228753
(Patent Document 2) Korean Patent Publication No. 10-1568495
An aspect of the present disclosure is to provide a hot-rolled steel sheet having excellent shape correction properties and a method for manufacturing the same.
According to an aspect of the present disclosure, a hot-rolled steel sheet is provided, the hot-rolled steel sheet including, by weight: 0.06 to 0.12% of C, 0.004 to 0.4% of Si, 0.8 to 2.0% of Mn, 0.01 to 0.05% of Al, 0.05 to 1.0% of Cr, 0.001 to 0.3% of Mo, 0.001 to 0.05% of P, 0.001 to 0.005% of S, 0.001 to 0.01% of N, 0.001 to 0.05% of Nb, 0.001 to 0.05% of Ti, 0.001 to 0.005% of B, with a remainder of Fe and other inevitable impurities, satisfying Relational Expression 1 below, and having a microstructure including, by area, 5 to 15% of austenite, 80% or more of auto-tempered martensite, and a remainder of at least one of bainite and ferrite.
According to another aspect of the present disclosure, a hot-rolled steel sheet is provided, the hot-rolled steel sheet including, by weight: 0.06 to 0.12% of C, 0.004 to 0.4% of Si, 0.8 to 2.0% of Mn, 0.01 to 0.05% of Al, 0.05 to 1.0% of Cr, 0.001 to 0.3% of Mo, 0.001 to 0.05% of P, 0.001 to 0.005% of S, 0.001 to 0.01% of N, 0.001 to 0.05% of Nb, 0.001 to 0.05% of Ti, 0.001 to 0.005% of B, with a remainder of Fe and other inevitable impurities, satisfying Relational Expression 1 below, and having a microstructure including, by area, 80% or more of auto-tempered martensite, and a remainder of at least one of fresh martensite, bainite, and ferrite, wherein a wave height of the steel sheet in a longitudinal direction is 10 nm or less.
According to another aspect of the present disclosure, a method for manufacturing a hot-rolled steel sheet is provided, the manufacturing method including: reheating a slab including by weight: 0.06 to 0.12% of C, 0.004 to 0.4% of Si, 0.8 to 2.0% of Mn, 0.01 to 0.05% of Al, 0.05 to 1.0% of Cr, 0.001 to 0.3% of Mo, 0.001 to 0.05% of P, 0.001 to 0.005% of S, 0.001 to 0.01% of N, 0.001 to 0.05% of Nb, 0.001 to 0.05% of Ti, 0.001 to 0.005% of B, with a remainder of Fe and other inevitable impurities, the slab satisfying Relational Expression 1 below, at a temperature within a range of 1200 to 1350° C.; hot rolling the reheated slab at a temperature within a range of 800 to 1200° C. to satisfy Relational Expression 2 below to obtain a hot-rolled steel sheet; and primarily cooling, secondarily cooling, and coiling the hot-rolled steel sheet to satisfy Relational Expressions 3 to 6.
FDT≥896−251[C]+37.5[Si]−31.6[Mn]−7.16[Cr]+29.5[Mo]+129[Ti]−107[Nb] [Relational Expression 2]
MTL≤MT≤MTU [Relational Expression 3]
CRL≤ICR [Relational Expression 4]
TCR≤80° C./sec [Relational Expression 5]
MTL−100≤CT [Relational Expression 6]
in the above Relational Expressions 2 to 6, where FDT refers to a surface temperature of the hot-rolled steel sheet at the end of hot rolling, MT refers to a surface temperature of the hot-rolled steel sheet at the end of primary cooling and the start of secondary cooling, MTL refers to 430−380[C]−13.4[Si]−47.3[Mn]−16.0[Cr]−24.2[Mo], MTU refers to 481−358[C]−16.6[Si]−45.6[Mn]−15.2[Cr]−24.1[Mo], ICR refers to a primary cooling rate of the surface of hot-rolled steel sheet from FDT to MT, CRL refers to 10[2.9−(0.1[C]+0.9[Mn]+0.5[Cr]+1.2[Mo])]+10, TCR refers to an average cooling rate of the surface of the hot-rolled steel sheet from FDT to CT, and CT refers to a coiling temperature.
According to another aspect of the present disclosure, a method for manufacturing a hot-rolled steel sheet is provided, the manufacturing method including: reheating a slab including by weight: 0.06 to 0.12% of C, 0.004 to 0.4% of Si, 0.8 to 2.0% of Mn, 0.01 to 0.05% of Al, 0.05 to 1.0% of Cr, 0.001 to 0.3% of Mo, 0.001 to 0.05% of P, 0.001 to 0.005% of S, 0.001 to 0.01% of N, 0.001 to 0.05% of Nb, 0.001 to 0.05% of Ti, 0.001 to 0.005% of B, with a remainder of Fe and other r inevitable impurities, the slab satisfying Relational Expression 1 below, at a temperature within a range of 1200 to 1350° C.; hot rolling the reheated slab at a temperature within a range of 800 to 1200° C. to satisfy Relational Expression 2 below to obtain a hot-rolled steel sheet; primarily cooling, secondarily cooling, and coiling the hot-rolled steel sheet to satisfy Relational Expressions 3 to 6; and leveling the coiled hot-rolled steel sheet.
MTL≤MT≤MTU [Relational Expression 3]
CRL≤ICR [Relational Expression 4]
TCR≤80° C./sec [Relational Expression 5]
MTL−100≤CT [Relational Expression 6]
in the above Relational Expressions 2 to 6, where FDT refers to a surface temperature of the hot-rolled steel sheet at the end of hot rolling, MT refers to a surface temperature of the hot-rolled steel sheet at the end of primary cooling and the start of secondary cooling, MTL refers to 430−380[C]−13.4[Si]−47.3[Mn]−16.0[Cr]−24.2[Mo], MTU refers to 481-358[C]−16.6[Si]−45.6[Mn]−15.2[Cr]−24.1[Mo], ICR refers to a primary cooling rate of the surface of hot-rolled steel sheet from FDT to MT, CRL refers to 10[2.9−(0.1[C]+0.9[Mn]+0.5[Cr]+1.2[Mo])]+10, TCR refers to an average cooling rate of the surface of the hot-rolled steel sheet from FDT to CT, and CT refers to a coiling temperature.
As set forth above, according to an aspect of the present disclosure, a high-strength hot-rolled steel sheet having excellent shape correction properties and a method for manufacturing the same can be provided.
In order to manufacture a hot-rolled steel sheet having high strength and excellent shape correction properties, the above-described properties should be simultaneously secured within a hot-rolling process without performing an additional heat treatment process. In general, in the case of a steel material having high strength, the steel material should include a low-temperature transformation phase such as martensite or bainite to secure the strength, and in order to secure such a low-temperature transformation phase, cooling should be performed at a high cooling rate and a low cooling stop temperature during the cooling process in the hot rolling process. However, in this case, a wave height of the hot-rolled steel sheet is significantly increased and yield strength also increases, so that it may be difficult to perform shape correction.
The present inventors had the insight that a hot-rolled steel sheet with high yield strength and excellent shape correction properties may be manufactured by precisely controlling alloy composition and manufacturing conditions, thereby completing the present invention.
Hereinafter, the present disclosure will be described. First, an alloy composition of the present disclosure will be described. A content of the alloy composition described below refers to % by weight.
Carbon (C) is the most economical and effective element in strengthening steel, and as an addition amount of C increases, a fraction of martensite or bainite increases, thereby increasing tensile strength and yield strength. In particular, the strength of tempered martensite or martensite is absolutely affected by the C content. If the C content is less than 0.06%, it is difficult to obtain a sufficient strengthening effect compared to the yield strength to be obtained by the present disclosure, and if the C content exceeds 0.12%, martensite becomes too hard, so that there is a problem of an increase in brittleness and a decrease in shape correction and in addition, there is a disadvantage in that weldability and material uniformity are also inferior. Therefore, the C content is preferably in the range of 0.06 to 0.12%. A lower limit of the C content is more preferably 0.065% and even more preferably 0.07%. An upper limit of the C content is more preferably 0.115%, and even more preferably 0.110%.
Silicon (Si) is an element which deoxidizes molten steel, exerts a solid solution strengthening effect within a matrix, and is advantageous in delaying formation of coarse carbides, concentrating C, and allowing austenite to remain even after cooling when certain cooling conditions are met. If the Si content is less than 0.004%, the effect of delaying the formation of carbides is not sufficient, so that not only is it difficult to retain austenite, but a process cost for controlling the Si content is also excessively required. If the Si content exceeds 0.4%, a red scale due to Si is formed on a surface of the steel sheet during hot rolling, which not only significantly deteriorates the surface quality of the steel sheet, but also deteriorates bendability and material uniformity, which ultimately leads to poor shape correction properties. Therefore, the Si content is preferably in the range of 0.004 to 0.4%. A lower limit of the Si content is more preferably 0.01%, even more preferably 0.03%, and most preferably 0.05%. An upper limit of the Si content is more preferably 0.25%, even more preferably 0.18%, and most preferably 0.15%.
Manganese (Mn), like Si, is an effective element in solid solution strengthening steel, and increases hardenability of steel to facilitate formation of a low-temperature transformation structure such as martensite and bainite during cooling. However, if the Mn content is less than 0.8%, the above-described effect is too low, and the burden of increasing alloy costs increases as the insufficient hardenability of steel is compensated for with other elements. On the other hand, if the Mn content exceeds 2.0%, a segregation zone is developed significantly in a thickness central portion during casting of a slab in a continuous casting process, and during cooling, the microstructure in a thickness direction is formed to be non-uniform, resulting in poor shape correction properties. In addition, grain boundaries may be weakened, thereby excessively increasing brittleness of steel. Therefore, the Mn content is preferably in the range of 0.8 to 2.0%. A lower limit of the Mn content is more preferably 0.9%. An upper limit of the Mn content is more preferably 1.8%, and even more preferably 1.7%.
Aluminum (Al) is an element mainly added for deoxidation of a steel material, and it the Al content is less than 0.01%, the above-described effect is insufficient. On the other hand, if the Al content exceeds 0.05%, Al combines with nitrogen (N) to form AlN, so that it is likely to cause corner cracks in a slab during continuous casting, and defects due to formation of inclusions, and which may have an adverse effect on shape correction. Therefore, the Al content is preferably in the range of 0.01 to 0.05%. A lower limit of the Al content is more preferably 0.015% and even more preferably 0.02%. An upper limit of the Al content is more preferably 0.045% and even more preferably 0.45%.
Chromium (Cr) strengthens steel by solid solution and increases hardenability of steel during cooling, to suppress formation of ferrite, and simultaneously, serves to help formation of a low-temperature transformation structure such as martensite or bainite. If the Cr content is less than 0.05%, the above-described effect cannot be achieved or becomes excessively small. On the other hand, when the content of Cr exceeds 1.0%, similarly to Mn, a segregation zone in a thickness central portion starts to be developed significantly, and the microstructure in a thickness direction becomes non-uniform, resulting in poor material uniformity and shape correction properties. In addition, the formation of bainite is promoted more than the formation of tempered martensite targeted by the present disclosure, making it difficult to secure strength. Therefore, the Cr content is preferably in the range of 0.05 to 1.0%. A lower limit of the Cr content is more preferably 0.07% and even more preferably 0.1%. An upper limit of the Cr content is more preferably 0.9%.
Molybdenum (Mo) increases hardenability of steel to facilitate formation of a low-temperature transformation structure such as martensite and bainite, which is known to be strong to be similar to that of Mn. However, unlike Mn, Mo strengths grain boundaries and suppress brittleness and serves to increase strength. If the Mo content is less than 0.001%, the above-described effect cannot be sufficiently obtained, and if the Mo content exceeds 0.3%, Mo combines with C formed during coiling after hot rolling to grow the precipitates coarsely, so that areas in which material uniformity and shape correction properties are partially deteriorated may occur. In addition, since Mo is an expensive element, it is disadvantageous in terms of manufacturing costs and is also harmful to weldability. Therefore, the Mo content is preferably in the range of 0.001 to 0.3%. A lower limit of the Mo content is more preferably 0.03%, more preferably 0.05%, and most preferably 0.07%.
Phosphorus (P) is an element having a high solid solution strengthening effect, but causing brittleness due to grain boundary segregation to deteriorate material uniformity and shape correction properties. If the P content exceeds 0.05%, as described above, sudden breakage, or the like may occur during shape correction due to the brittleness due to grain boundary segregation, which may result in poor shape correction properties. It is advantageous to control the P content as low as possible. However, if the P content is less than 0.001%, a lot of manufacturing costs are required, which is economically disadvantageous. Therefore, the P content is preferably in the range of 0.001 to 0.05%.
A lower limit of the P content is more preferably 0.002%, more preferably 0.003%, and most preferably 0.005%. An upper limit of the P content is more preferably 0.03%, more preferably 0.02%, and most preferably 0.015%.
Sulfur (S) is an impurity which exists in steel, and when the S content exceeds 0.005%, S combines with Mn to form non-metallic inclusions, which may cause a problem in that microcracks to easily occur and impact resistance is greatly reduced during bending steel, and material uniformity and shape correction properties are deteriorated. On the other hand, it is advantageous to control the S content to be as low as possible, but if the S content is less than 0.001%, a lot of time and energy are required during steelmaking, which reduces productivity. Therefore, the S content is preferably in the range of 0.001 to 0.005%. A lower limit of the S content is more preferably 0.002%. An upper limit of the S content is more preferably 0.0004%.
Nitrogen (N), together with C, is a representative solid solution strengthening element, and also forms coarse precipitates together with Ti, Al, or the like. In general, it is known that the solid solution strengthening effect of N is superior to that of carbon. However, if the N content exceeds 0.01%, there is a problem in that toughness is greatly reduced. On the other hand, if the N content is less than 0.001%, a lot of time is required during steelmaking operation, which reduces productivity. Therefore, the N content is preferably in the range of 0.001 to 0.01%. A lower limit of the N content is more preferably 0.002%, even more preferably 0.003%, and most preferably 0.004%. An upper limit of the N content is more preferably 0.009% and even more preferably 0.008%.
Niobium (Nb) is a representative precipitation strengthening element together with Ti and V, effective in improving strength and impact toughness through a grain refinement effect due to delayed recrystallization by precipitation during hot rolling. In addition, it is advantageous to retain austenite under specific cooling conditions. As these physical properties increase, shape correction properties can be improved. If the Nb content is less than 0.001%, the above-described effect cannot be obtained. On the other hand, if the Nb content exceeds 0.05%, Nb is grown into coarse composite precipitates, which has the problem of deteriorating material uniformity. Therefore, the Nb content is preferably in the range of 0.001 to 0.05%. An upper limit of the Nb content is more preferably 0.03%, even more preferably 0.02%, and most preferably 0.01%.
Titanium (Ti) is a representative precipitation strengthening element along with Nb and V, and forms TiN due to the strong affinity with N. TiN has the effect of suppressing growth of grains during a heating process for hot rolling, which is advantageous in utilizing B added to improve hardenability through stabilization of dissolved N. In addition, Ti remaining after reacting with nitrogen is dissolved in steel and combined with carbon to form TiC precipitates, which is a useful ingredient in additionally improving the strength of steel. If the Ti content is less than 0.001%, the above-described effect cannot be obtained. On the other hand, if the Ti content exceeds 0.05%, there is a problem of poor material uniformity due to the generation of coarse TiN and coarsening of precipitates during a heat treatment. Therefore, the Ti content is preferably in the range of 0.001 to 0.05%. A lower limit of the Ti content is more preferably 0.005%, even more preferably 0.01%, and most preferably 0.02%. An upper limit of the Ti content is more preferably 0.04% and even more preferably 0.03%.
Boron (B) has the effect of improving hardenability when exists in a solid solution state in steel, has the effect of improving brittleness of steel in low-temperature areas by stabilizing grain boundaries, and has the effect of strengthening grain boundaries even in a trace amount thereof. If the B content is less than 0.001%, it is difficult to obtain the above-described effect. On the other hand, if B content exceeds 0.005%, the hardenability increases significantly, resulting in poor formability, and the formation of precipitates such as coarse BN occurs, which actually increases the brittleness of steel. Therefore, the B content is preferably in the range of 0.001 to 0.005%. An upper limit of the B content is more preferably 0.004%, and even more preferably 0.003%.
Meanwhile, it is preferable that the hot-rolled steel sheet of the present disclosure satisfies the above-described alloy composition, and simultaneously satisfies the following Relational Expression 1 (hereinafter, a left side thereof in the following Relational Expression 1 is also referred to as ‘T’). In this case, a content of each alloy element in the following Relational Expression 1 is % by weight.
The above Relational Expression 1 is a component Relational Expression for controlling a microstructure. When the T value exceeds 20, a sufficient low-temperature structure is obtained, but non-uniform distribution of a Mn segregation zone and retained austenite increases, making it impossible to obtain uniform physical properties, which cannot obtain a sufficient shape correction effect. Therefore, the T value is preferably 20 or less. The T value is more preferably 19 or less, even more preferably 17 or less, and most preferably 16 or less. Meanwhile, the smaller the T value, the more advantageous it is to secure a uniform microstructure and physical properties, so in the present disclosure, a lower limit of the T value is not particularly limited.
The remaining component of the present disclosure is iron (Fe). However, since in the common manufacturing process, unintended may be inevitably impurities incorporated from materials or raw the surrounding environment, the component may not be excluded. Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.
In this case, the inevitable impurities may include 0.01% or less of Ni. Ni is an expensive element, and in the present disclosure, excellent shape correction properties may be secured without adding Ni, so it has the advantage of excellent economic efficiency. The Ni content is more preferably 0.008% or less, even more preferably 0.006% or less, and most preferably 0.005% or less.
It is preferable that the hot-rolled steel sheet of the present disclosure includes a microstructure before shape correction through leveling, by area, at last one of 5 to 15% of austenite, 80% or more of auto-tempered martensite, and a remainder of at least one of bainite and ferrite. Austenite lowers a yield strength and improves shape correction, and simultaneously, is transformed into martensite after leveling, thereby improving strength. When the austenite fraction is less than 5%, it is difficult to sufficiently obtain the above-described effect, and when the austenite fraction exceeds 15%, a sufficient low-temperature structure may not be secured, which has the disadvantage of lowering the strength of the finally obtained steel sheet. A lower limit of the austenite fraction is more preferably 6%, and even more preferably 7%. An upper of the austenite fraction is more preferably 13%, even more preferably 11%, and most preferably 10%. Auto-tempered martensite has ductility which is advantageous for localized and limited transformation, such as shape correction, and has the effect of having high strength. When the auto-tempered martensite fraction is less than 80%, there is a disadvantage in that the strength of the finally obtained steel sheet excessively low. The auto-tempered martensite fraction is more preferably 82% or more. Auto-tempered martensite is more advantageous in securing strength if auto-tempered martensite is formed in as large a quantity as possible, but at least one of bainite and ferrite may inevitably be formed during the manufacturing process. Meanwhile, auto-tempered martensite has almost the same structure as tempered martensite, which is formed through short-term tempering at a low temperature without performing separate tempering, and has fine epsilon carbides formed within a lath.
It is preferable that the hot-rolled steel sheet of the present disclosure includes a microstructure after shape correction through leveling, by area: at least one of 80% or more of auto-tempered martensite, and a remainder of at least one of fresh martensite, bainite, and ferrite. Austenite before leveling is transformed into martensite after leveling, not only shape correction but also superior strength can be secured.
In addition, the hot-rolled steel sheet of the present disclosure after leveling has excellent shape correction properties as a wave height of the steel sheet in a longitudinal direction is 10 mm or less. In this case, the wave height refers to a height from the valley to the crest when the steel sheet has a wave shape in the longitudinal direction.
The hot-rolled steel sheet before and after leveling, provided as described above preferably has an average grain size of prior austenite of 10 to 30 μm. When the average grain size of the prior austenite is less than 10 μm, there is a disadvantage in that quenchability is reduced and a sufficient low-temperature structure cannot be secured. When the average grain size of the prior austenite exceeds 30 μm, there is a disadvantage in that retained austenite cannot be formed in the steel sheet due to excessively increased quenchability and ductility is greatly reduced. A lower limit of the average grain size of prior austenite is more preferably 12 μm, even more preferably 15 μm, and most preferably 17 μm. An upper limit of the average grain size of prior austenite is more preferably 28 μm and even more preferably 26 μm.
In addition, the hot-rolled steel sheet after leveling may have excellent strength with a yield strength of 900 MPa or more.
Hereinafter, a method for manufacturing a hot-rolled steel sheet according to an embodiment of the present disclosure will be described. Meanwhile, the method for manufacturing a hot-rolled steel sheet according to an embodiment of the present disclosure may also be performed using a process in which continuous casting and hot rolling processes are directly connected.
First, a slab satisfying the above-described alloy composition and Relational Expression 1 is reheated at a temperature within a range of 1200 to 1350° C. When the reheating is lower than 1200° C., precipitates are not sufficiently re-dissolved, so the formation of is reduced in processes after hot rolling, coarse TiN remains, and it is difficult to eliminate segregation generated during continuous casting by diffusion. On the other hand, when the reheating is higher than 1350° C., the strength decreases and tissue non-uniformity occurs due to abnormal grain growth of austenite grains, so the reheating temperature is preferably in the range of 1200 to 1350° C. A lower limit of the reheating temperature is more preferably 1220° C., even more preferably 1230° C., and most preferably 1250° C. An upper limit of the reheating temperature is more preferably 1330° C., even more preferably 1310° C., and most preferably 1300° C.
Thereafter, the reheated slab is hot rolled at a temperature within a range of 800 to 1200° C. satisfy the following Relational Expression 2 to obtain a hot-rolled steel sheet. When the hot rolling temperature is higher than 1200° C., a temperature of the hot-rolled steel sheet increases, the grain size becomes coarse, and surface quality of the hot-rolled steel sheet deteriorates. On the other hand, when the hot rolling temperature is lower than 800° C., stretched crystal grains are developed due to excessive recrystallization delay, which worsens anisotropy and deteriorates formability, ultimately deteriorating material uniformity and shape correction properties. A lower limit of the hot rolling temperature is more preferably 810° C., even more preferably 820° C., and most preferably 830° C. An upper limit of the hot rolling temperature is more preferably 1180° C.
Meanwhile, in the present disclosure, it is preferable to satisfy the conditions of the following Relational Expression 2 (hereinafter, a right side thereof in the following Relational Expression 2 is also referred to as ‘FDTL’) during hot rolling. In the following Relational Expression 2, FDT refers to a surface temperature of the hot-rolled steel sheet at the end of hot rolling.
When the FDT is lower than FDTL, ferrite is partially formed on a surface of a steel sheet of which the temperature is lower than that of a thickness central portion of the steel sheet, so a sufficient fraction of martensite is not formed after cooling, resulting in material deviation between the central portion and the surface portion, thereby causing a problem in that shape correction properties are also inferior. In other words, if Relational Expression 2 is satisfied, high strength and excellent shape correction properties can be obtained simultaneously.
Thereafter, the hot rolled steel sheet is primarily cooled, secondarily cooled, and coiled to satisfy the following Relational Expressions 3 to 6. In this case, in the following Relational Expressions 3 to 6, MT a surface temperature of the hot-rolled steel sheet at the end of primary cooling and at the start of secondary cooling, MTL refers to 430−380[C]−13.4[Si]−47.3[Mn]−16.0[Cr]−24.2[Mo], MTU refers to 481−358[C]−16.6[Si]−45.6[Mn]−15.2[Cr]−24.1[Mo], ICR refers to a primary cooling rate on a surface of the hot-rolled steel sheet from FDT to MT, CRL refers to 10[2.9−(0.1[C]+0.9[Mn]+0.5[Cr]+1.2[Mo])]+10, TCR refers to an average cooling rate of the surface of the hot-rolled steel sheet from FDT to CT, and CT refers to a coiling temperature.
When the MT exceeds MTU, martensite cannot be formed, and when the MT is less than the MTL, fine and evenly distributed austenite cannot be formed. When the ICR is lower than the CRL, sufficient martensite cannot be formed, and a large amount of ferrite or bainite is formed unintentionally, making it impossible to obtain h strength, thereby suppressing the formation of austenite, which also deteriorates shape correction properties. Meanwhile, in the present disclosure, even if the value of ICR is very high, there is no significant change in the strength of martensite, so an upper limit thereof is not particularly limited. If the TCR exceeds 80° C./sec, a problem occurs in which austenite is exposed to low temperatures and disappears before being stabilized. If the CT is lower than MTL-100, a temperature of a coil becomes too low, causing a difficulty in coiling during the process. In addition, as fine residual austenite formed in a process of generating a large amount of martensite phases, which is excessively hard and poorly brittle, disappears, the material of the rolled sheet becomes non-uniform and the shape deteriorates. Meanwhile, in the present disclosure, an upper limit of the coiling temperature is not particularly limited, but in terms of securing strength, the upper limit thereof may be 350° C. In other words, the fine and evenly distributed austenite formed by appropriately controlling the cooling and coiling processes makes correction easier during shape correction through leveling, and simultaneously, all the austenite after correction disappears. The steel hot-rolled sheet manufactured through the above-described process control may have excellent shape correction properties and high yield strength.
Thereafter, leveling the coiled hot-rolled steel sheet may be included. The leveling is performed for shape correction, and in the present disclosure, the leveling process is not particularly limited, and all conventional techniques used in the art may be used. Meanwhile, the leveling is a shape correction method in which reduction is not applied to a steel sheet, and thus, it can be distinguished from skin pass rolling in which a rolling reduction of 0.1 to 2.0% is applied.
Hereinafter, the present disclosure will be specifically described through the following Examples. However, it should be noted that the following examples are only for describing the present disclosure by illustration, and not intended to limit the right scope of the present disclosure. The reason is that the right scope of the present disclosure is determined by the matters described in the claims and reasonably inferred therefrom.
A slab having the alloy composition shown in Table 1 below was reheated under the conditions shown in Table 2 below to manufacture a hot-rolled steel sheet. In this case, a reheating temperature of the slab was 1250° C., and a thickness of the hot-rolled steel sheet immediately after hot rolling was 4 mm. Thereafter, leveling was performed using a tension leveler. A microstructure, average particles size of prior austenite, wave height, and mechanical properties for a hot-rolled steel sheet before and after levelling, and the results thereof were shown in Table 3 and 4 below, respectively. Meanwhile, in this example, a trace amount of impurities was detected even though Ni was not added.
The microstructure was measured using an Electron Back-Scattered Diffraction (EBSD) test equipment of an electron microscope.
The average particle size of prior austenite was measured by mixing 200 ml of supersaturated aqueous picric acid solution and 10 ml of 10% aqueous sodium dodecylbenzene sulfonate solution, and corroding a specimen collected from the hot-rolled steel sheet manufactured above for 10 minutes in a mixed solution obtained by adding 10 ml of 10% aqueous ferric chloride solution with an optical microscope.
The wave height was expressed as the largest difference from a valley to a crest for a steel sheet length of 2 m after unwinding the hot-rolled coil.
Yield strength (YS), tensile strength (TS), and elongation at break (El) were measured by collecting JIS 5 standard test specimens from the hot-rolled coil in a direction parallel to a rolling direction.
As can be seen from Tables 1 to 4 above, in Inventive Examples 1 to 6 satisfying all of the alloy composition, relational expressions, and manufacturing conditions proposed by the present disclosure, it can be seen that the mechanical properties and shape quality targeted by the disclosure are secured.
In Comparative Example 1, the manufacturing conditions of the present disclosure are satisfied, but the range of the C content of the present disclosure is exceeded and Relational Expression 1 is not satisfied, so it can be seen that the wave height after leveling is high due to high strength and low shape correction properties.
In Comparative Example 2, the manufacturing conditions of the present disclosure are satisfied, but the range of the C content of the present disclosure is felt below, so it can be seen that the yield strength is low.
In Comparative Example 3, the manufacturing conditions of the present disclosure are satisfied, but the range of the Mn content of the present disclosure is exceeded and Relational Expression 1 is not satisfied, which leads to a deterioration in shape correction properties due to increased segregation and embrittlement, so it can be seen that the wave height after leveling is high.
In Comparative Example 4, the manufacturing conditions of the present disclosure are satisfied, but the range of the C and Cr contents of the present disclosure is felt below and Relational Expression 1 is not satisfied, so it can be seen that the yield strength is low and the wave height after leveling is high.
In Comparative Example 5, the alloy composition of the present disclosure is satisfied, but not only is the existing hot rolling process using one-stage cooling adopted, but MT does not satisfy the conditions of the present disclosure, so it can be seen that an appropriate fraction of austenite before leveling may not be secured, and the yield strength is also low.
In Comparative Example 6, the C content range of the present disclosure is exceeded and FDT is lower than FDTL, so it can be seen that anisotropy increases due to ferrite formed during rolling, the yield strength is low due to material non-uniformity, and the wave height after leveling is high.
In Comparative Example 7, the alloy composition of the present disclosure is satisfied, but CT does not satisfy the conditions of the present disclosure, so it can be seen that an appropriate fraction of austenite cannot be secured before leveling, and a wave height after leveling is high.
In Comparative Example 8, the alloy composition of the present disclosure is satisfied, but it can be seen that the yield strength is low as ICR is lower than CRL.
In Comparative Example 9, the alloy composition of the present disclosure is satisfied, but as TCR exceeds the conditions of the present disclosure, so it can be seen that an appropriate fraction of austenite cannot be secured before leveling, and a wave height after leveling is high.
In Example 10, the manufacturing conditions of the present disclosure are satisfied, but Relational Expression 1 is not satisfied, so it can be seen that a wave height after leveling is high.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2021-0161314 | Nov 2021 | KR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/KR2022/017335 | 11/7/2022 | WO |
