Patent Application
20160060723
This disclosure relates to a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more which can be preferably used as a material for structural parts and skeleton members of automobiles or frames of trucks and, in particular, relates to improvement of bending workability.
Nowadays, automobile exhaust gas regulations are being strengthened from the viewpoint of global environment conservation. In such a situation, since the improvement of the fuel efficiency of automobiles such as trucks is an important problem to be solved, there is a growing demand for the strengthening and thickness reduction of materials used for automobiles. Therefore, there is a tendency toward actively using high-strength hot-rolled steel sheets as materials for automotive parts, and demands for high-strength hot-rolled steel sheets are increasing year by year. In particular, a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more is highly anticipated to serve as a material which significantly improves the fuel efficiency of automobiles.
Generally, however, an increase in the strength of a steel sheet is accompanied by a decrease in bending workability. Therefore, various investigations have been conducted to provide bending workability required for a material for automotive parts to a high-strength hot-rolled steel sheet.
For example, Japanese Unexamined Patent Application Publication No. 2012-062558 proposes a technology to manufacture a hot-rolled steel sheet, the technology including heating and holding a steel material having a chemical composition containing, by mass %, C: 0.05% to 0.15%, Si: 0.2% to 1.2%, Mn; 1.0% to 2.0%, P: 0.04% or less, S: 0.0030% or less, Al: 0.005% to 0.10%, N: 0.005% or less, Ti: 0.03% to 0.13%, and the balance being Fe and inevitable impurities at a temperature of 1200° C. to 1350° C. for 1200 seconds or more, then hot-rolling the heated material under the conditions that the finishing temperature of rough rolling is 1050° C. or higher and the finishing temperature of finish rolling is 830° C. to 930° C., and thereafter cooling the hot-rolled steel sheet at an average cooling rate of 35° C./s or more to a coiling temperature of 350° C. to 550° C.
According to the technology proposed in Japanese Unexamined Patent Application Publication No. 2012-062558, it is possible to obtain a hot-rolled steel sheet having a microstructure including, in terms of area fraction, less than 80% of a bainite phase and 10% or more of a ferrite phase having a grain diameter of 2 to 15 μm in surface regions which are respectively within 1.5 to 3.0% of the whole thickness of the steel sheet from both surfaces of the steel sheet and including, in terms of area fraction, more than 95% of a bainite phase in an inner region which is a region other than the surface regions. According to the technique proposed in Japanese Unexamined Patent Application Publication No. 2012-062558, by forming the soft microstructure described above in the surface regions, it is possible to obtain a high-strength hot-rolled steel sheet excellent in bending workability having a tensile strength of 780 MPa or more.
Japanese Unexamined Patent Application Publication No. 2009-270142 proposes a technology to manufacture a hot-rolled steel sheet, the technique including heating a steel slab having a chemical composition containing, by mass %, C: 0.05% to 0.19%, Si: 0.05% to 1.0%, Mn: 0.3% to 2.5%, P: 0.03% or less, S: 0.025% or less, Ti: 0.005% to 0.1%, Cr: 0.03% to 1.0%, Sol.Al: 0.005% to 0.1%, N: 0.0005% to 0.01%, B: 0.0001% to 0.01%, and the balance being Fe and inevitable impurities, in which the relationship 3C≦0.27Mn+0.2Cr+0.05Cu+0.11Ni+0.25Mo≦3C+0.3 (C, Mn, Cr, Cu, Ni, Mo are represented in units of mass %), at a temperature of 1070° C. or higher and 1300° C. or lower, then hot-rolling the heated slab under the condition that the finishing temperature is 850° C. or higher and 1070° C. or lower, and thereafter cooling the hot-rolled steel sheet to a temperature of 300° C. or lower at a cooling rate VC (° C./sec) which satisfies the relationship 1.2/C≦VC≦1.8/C (C is represented in units of mass %).
According to the technology proposed in Japanese Unexamined Patent Application Publication No. 2009-270142, it is possible to obtain a hot-rolled steel sheet composed of a surface layer thereof having a microstructure including, in terms of area fraction, 80% or more of a bainite phase, a Vickers hardness Hv of 210 or more and 300 or less, an average value of the lengths of the major axis of bainite grains of 5 μm or less, and an average grain boundary carbide diameter of 0.5 μm or less. According to the technology proposed in Japanese Unexamined Patent Application Publication No. 2009-270142, it is possible to obtain a hot-rolled steel sheet for a steel pipe used for a machinery structure excellent in terms of fatigue resistance and bending workability by controlling the microstructure in the surface layer of the steel sheet to be uniform and fine and to include mainly a bainite structure to have an intermediate hardness and by decreasing the size of grain boundary precipitated carbides.
However, in Japanese Unexamined Patent Application Publication No. 2012-062558, since it is not always possible to obtain a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more, there is room for improvement.
In Japanese Unexamined Patent Application Publication No. 2009-270142, since the microstructure of a steel sheet is controlled by setting a cooling stop temperature to be 300° C. or lower and by adjusting mainly a cooling rate, it can be difficult to stably achieve the desired microstructure of a steel sheet due to a variation in cooling rate in mass production. Moreover, in the technique proposed in Japanese Unexamined Patent Application Publication No. 2009-270142, since the cooling stop temperature is set to 300° C. or lower, there is a tendency for a hard microstructure to be formed in the surface regions of a steel sheet, which results in a situation where it is not possible to provide a hot-rolled steel sheet with sufficient bending workability.
It could thus be helpful to provide a high-strength hot-rolled steel sheet having a high tensile strength of 980 MPa or more and excellent bending workability which has, in particular, a thickness of 3.2 mm or more and 14 mm or less and a method of manufacturing the steel sheet.
We thus provide:
[1] A high-strength hot-rolled steel sheet excellent in bending workability, the steel sheet comprising:
a chemical composition containing, by mass %, C: more than 0.1% and 0.2% or less, Si: 0.5% or more and 3.0% or less, Mn: 1.0% or more and 3.5% or less, P: 0.05% or less, S: 0.004% or less, Al: 0.10% or less, N: 0.008% or less, Ti: 0.05% or more and 0.15% or less, V: more than 0.10% and 0.30% or less, and the balance being Fe and inevitable impurities,
surface regions including mainly a ferrite phase, and an inner region including mainly a bainite phase,
the surface regions having a microstructure including mainly a ferrite phase in an amount of 80% or more in terms of area fraction and the balance being at least one selected from among a bainite phase, a martensite phase, and a retained austenite phase in an amount of 0% or more and 20% or less in terms of area fraction,
the inner region having a microstructure including mainly a bainite phase in an amount of more than 90% in terms of area fraction and the balance being at least one selected from among a ferrite phase, a martensite phase, and a retained austenite phase in an amount of 0% or more and less than 10% in terms of area fraction, and
the proportions of the surface regions in the thickness direction of the steel sheet being 1.0% or more and 5.0% or less of the whole thickness respectively from the upper and lower surfaces of the steel sheet.
[2] The high-strength hot-rolled steel sheet excellent in bending workability according to item [1], wherein the chemical composition further contains, by mass %, at least one selected from the group consisting of Nb: 0.003% or more and 0.2% or less, B: 0.0002% or more and 0.0015% or less, Cu: 0.005% or more and 0.2% or less, Ni: 0.005% or more and 0.2% or less, Cr: 0.005% or more and 0.2% or less, and Mo: 0.005% or more and 0.2% or less.
[3] The high-strength hot-rolled steel sheet excellent in terms of bending workability according to item [1] or [2], wherein the chemical composition further contains, by mass %, at least one selected from the group consisting of Ca: 0.0002% or more and 0.01% or less and REM: 0.0002% or more and 0.01% or less.
[4] A method of manufacturing a high-strength hot-rolled steel sheet excellent in bending workability, the method including:
heating a steel slab having the chemical composition according to any one of items [1] to [3] in a temperature range of 1250° C. or higher,
holding the heated steel slab in the temperature range for 3600 seconds or more,
performing hot rolling including rough rolling and finish rolling under the condition that the finish delivery temperature is 840° C. or higher and 940° C. or lower,
starting cooling immediately after hot rolling has been performed,
performing cooling at an average cooling rate of 25° C./s or more, and
performing coiling at a coiling temperature of 350° C. or higher and 500° C. or lower.
It is possible to obtain a high-strength hot-rolled steel sheet having a tensile strength of 980 MPa or more and excellent in bending workability. Therefore, when our steel sheets are applied to the structural parts and skeleton members of automobiles, the frames of trucks and the like, it is possible to reduce auto weight while maintaining automotive safety and it is possible to reduce environmental loads. In addition, it is possible to stably manufacture a hot-rolled steel sheet having increased bending workability while maintaining a high strength of 980 MPa or more in terms of tensile strength, which has a marked effect on industry.
We conducted investigations for the purpose of increasing the bending workability of a hot-rolled steel sheet while maintaining a high strength of 980 MPa or more in terms of tensile strength TS. We found that it is very effective to form a microstructure including mainly a ferrite phase in the surface regions of a hot-rolled steel sheet and a microstructure including mainly a bainite phase in the region other than the surface regions (inner region) of the hot-rolled steel sheet to achieve a satisfactory strength-bending workability balance of the hot-rolled steel sheet. In addition, we found that there is a significant increase in the bending workability of a hot-rolled steel sheet while maintaining a high strength TS of 980 MPa or more in terms of tensile strength by controlling the area fraction of a ferrite phase in surface regions and a bainite phase in an inner region and by controlling the proportions of surface regions in the thickness direction of a steel sheet.
We also conducted investigations regarding a method of forming the desired microstructure for a hot-rolled steel sheet described above, that is, a method of forming a microstructure including mainly a bainite phase with a specified amount of ferrite phase being formed in surface regions of the hot-rolled steel sheet. We conceived of heating a steel material at a temperature of 1250° C. or higher and holding the heated steel material at the heating temperature for 3600 seconds or more when a hot-rolled steel sheet is manufactured by heating steel material with a specified chemical composition and then by hot-rolling the heated steel material.
When a steel material is held in a high temperature range for a long time, the surface of the steel material is decarburized. In addition, the lower the C content of steel, the more the ferrite phase is likely to be formed. Therefore, we conducted experiments to make the amount of a ferrite phase formed in the surface regions of a hot-rolled steel sheet larger than that in a region other than the surface regions of the hot-rolled steel sheet in cooling and coiling processes after hot rolling has been performed by using the decarburizing mentioned above to decarburize the surface regions of the steel material in a heating process of the steel material. As a result, we found that, by heating a steel material at a temperature of 1250° C. or higher and by holding the heated steel material at the heating temperature for 3600 seconds or more, it is possible to obtain a hot-rolled steel sheet having the desired microstructure after cooling and coiling have been performed after hot rolling has been performed. As described above, we found that, by utilizing decarburization, it is possible to stably achieve the desired microstructure in the surface regions of a hot-rolled steel sheet.
Our steel sheets and methods will be described in detail hereafter.
First, the reasons for the limitations on the chemical composition of the hot-rolled steel sheet will be described. Hereinafter, % used when describing a chemical composition always represents mass %, unless otherwise noted.
C: More than 0.1% and 0.2% or Less
C increases the strength of steel and promotes formation of a bainite phase. Accordingly, it is necessary that the C content be more than 0.1%. On the other hand, when the C content is more than 0.2%, since it is difficult to control formation of a bainite phase, there is an increase in the amount of a martensite phase, which is a hard phase, resulting in a decrease in bending workability of the hot-rolled steel sheet. Therefore, the C content is more than 0.1% and 0.2% or less, or preferably 0.12% or more and 0.18% or less.
Since Si suppresses formation of large-size oxides and cementite, which decrease bending workability, and since Si facilitates formation of a ferrite phase, which improves bending workability, it is effective to add Si in an amount of 0.5% or more. In addition, Si is a chemical element which contributes to solute strengthening. On the other hand, when the Si content is more than 3.0%, since there is a significant decrease in the surface quality of a hot-rolled steel sheet, there is a decrease in phosphatability and corrosion resistance. Therefore, the Si content is 0.5% or more and 3.0% or less, preferably 0.5% or more and 2.5% or less, more preferably 0.6% or more and 2.0% or less, or further more preferably 0.7% or more.
Mn is one of the most important constituent chemical elements. Mn is a chemical element which increases the strength of steel by forming a solid solution and promotes formation of a bainite phase through increasing hardenability. It is necessary that the Mn content be 1.0% or more to realize such effects. Since Mn is a chemical element which tends to be concentrated in the central portion of a slab when slab casting is performed, it is possible to realize an increase in strength due to this concentration while keeping satisfactory bending workability for the surface regions of a hot-rolled steel sheet. On the other hand, when the Mn content is more than 3.5%, since there is also an increase in the Mn concentration in the surface regions, there is a deterioration in bending workability of the hot-rolled steel sheet. Therefore, the Mn content is 1.0% or more and 3.5% or less, preferably 1.5% or more and 3.0% or less, or more preferably more than 2.0% and 2.5% or less.
Although P is a chemical element which contributes to an increase in the strength of steel by forming a solid solution, P is a chemical element which also causes a decrease in low-temperature toughness and workability as a result of being segregated at grain boundaries, in particular, at prior-austenite grain boundaries. Therefore, it is preferable that the P content be as small as possible, but it is acceptable that the P content be 0.05% or less. Therefore, the P content is 0.05% or less. However, since it is not possible to realize an effect corresponding to an increase in the refining costs when the P content is excessively decreased, it is preferable that the P content be 0.003% or more and 0.03% or less, or more preferably 0.005% or more and 0.02% or less.
S decreases the workability of a hot-rolled steel sheet as a result of combining with Ti and Mn to form large-size sulfides. Therefore, it is preferable that the S content be as small as possible, but it is acceptable that the S content be 0.004% or less. Therefore, the S content is 0.004% or less. However, since it is not possible to realize an effect corresponding to an increase in the refining costs when the S content is excessively decreased, it is preferable that the S content be 0.0003% or more and 0.004% or less.
Al is a chemical element effective to increase the cleanness of steel by functioning as a deoxidizing agent. On the other hand, when the Al content is excessively large, there is an increase in the amount of oxide inclusions, which results in a decrease in the toughness of a hot-rolled steel sheet and results in the occurrence of defects. Therefore, the Al content is 0.10% or less, preferably 0.005% or more and 0.08% or less, or more preferably 0.01% or more and 0.05% or less.
N contributes to make a crystal grain size fine by being precipitated as the (form of) nitrides combining with nitride-forming elements. However, since N tends to combine with Ti to form large-size nitrides at a high temperature, there is a decrease in the bending workability of a hot-rolled steel sheet. Therefore, it is preferable that the N content be as small as possible. Therefore, the N content is 0.008% or less, preferably 0.001% or more and 0.006% or less, or more preferably 0.002% or more and 0.005% or less.
Ti: 0.05% or More and 0.15% or Less
Ti is one of the most important constituent chemical elements. Ti contributes to an increase in the strength of steel through making a crystal grain size fine as a result of forming carbonitrides and through precipitation strengthening. In addition, Ti has a role in improving the bending workability of a hot-rolled steel sheet by decreasing the amount of cementite in steel as a result of forming a large number of fine clusters of (Ti, V)C at a low temperature of 300° C. or higher and 450° C. or lower. It is necessary that the Ti content be 0.05% or more to realize such effects. On the other hand, when the Ti content is more than 0.15%, the effects described above become saturated. In addition, when the Ti content is more than 0.15%, since large-size TiCs are left undissolved in steel when a slab is heated, there is a decrease in the bending workability of a hot-rolled steel sheet, and there is a decrease in the amount of solid solute C before bainite transformation occurs, which results in a decrease in the strength of a steel sheet. Therefore, the Ti content is 0.05% or more and 0.15% or less, or preferably 0.08% or more and 0.13% or less.
V: More than 0.10% and 0.30% or Less
V is one of the most important constituent chemical elements. V contributes to an increase in the strength of steel through making a crystal grain size fine as a result of forming carbonitrides and through precipitation strengthening. V increases hardenability, and V contributes to formation of a bainite phase and to refine a bainite phase. V has a role in improving the bending workability of a hot-rolled steel sheet by decreasing the amount of cementite in steel as a result of forming a large number of fine clusters of (Ti, V)C at a low temperature of 300° C. or higher and 450° C. or lower. It is necessary that the V content be more than 0.10% to realize such effects. On the other hand, when the V content is more than 0.30%, there is a decrease in the ductility of a hot-rolled steel sheet, and there is an increase in cost. Therefore, the V content is more than 0.10% and 0.30% or less, or preferably 0.15% or more and 0.25% or less.
Although the chemical composition described above is the basic chemical composition of the hot-rolled steel sheet, the hot-rolled steel sheet may contain, as needed, at least one selected from the group consisting of Nb: 0.003% or more and 0.2% or less, B: 0.0002% or more and 0.0015% or less, Cu: 0.005% or more and 0.2% or less, Ni: 0.005% or more and 0.2% or less, Cr: 0.005% or more and 0.2% or less, and Mo: 0.005% or more and 0.2% or less, for example, to increase hole expansion formability or to increase strength.
Nb is a chemical element which contributes to an increase in the strength of steel through formation of carbonitrides. It is preferable that the Nb content be 0.003% or more to realize such an effect. On the other hand, when the Nb content is more than 0.2%, since there is an increase in deformation resistance, there is an increase in rolling force in hot rolling when a hot-rolled steel sheet is manufactured, which results in concern that the rolling operation may be difficult to perform due to an excessive increase in the load placed on a rolling mill. In addition, when the Nb content is more than 0.2%, there is a tendency for the workability of a hot-rolled steel sheet to decrease due to formation of large-size precipitates. Therefore, it is preferable that the Nb content be 0.003% or more and 0.2% or less, more preferably 0.01% or more and 0.15% or less, or further more preferably 0.015% or more and 0.1% or less.
B is a chemical element which inhibits formation and growth of a ferrite phase as a result of being segregated at austenite grain boundaries. Also, B is a chemical element which contributes to improve hardenability and forming a bainite phase and refining a bainite phase. It is preferable that the B content be 0.0002% or more to realize such effects. However, when the B content is more than 0.0015%, since formation of a martensite phase is promoted, there is a possibility that there may be a significant deterioration in the bending workability of a hot-rolled steel sheet. Therefore, when B is added, it is preferable that the B content be 0.0002% or more and 0.0015% or less, or more preferably 0.0004% or more and 0.0012% or less.
Cu is a chemical element which contributes to an increase in the strength of steel by forming a solid solution. In addition, Cu is a chemical element having a function of increasing hardenability, which, in particular, decreases the bainite transformation temperature, and which contributes to decreasing the grain size of a bainite phase. It is preferable that the Cu content be 0.005% or more to realize such effects. However, when the Cu content is more than 0.2%, there is a decrease in the surface quality of a hot-rolled steel sheet. Therefore, it is preferable that the Cu content be 0.005% or more and 0.2% or less, or more preferably 0.01% or more and 0.15% or less.
Ni is a chemical element which contributes to an increase in the strength of steel by forming a solid solution. In addition, Ni has a function of increasing hardenability and facilitates formation of a bainite phase. It is preferable that the Ni content be 0.005% or more to realize such effects. However, when the Ni content is more than 0.2%, since a martensite phase tends to be formed, there is a possibility that there may be a significant deterioration in the hole expansion formability of a hot-rolled steel sheet. Therefore, it is preferable that the Ni content be 0.005% or more and 0.2% or less, or more preferably 0.01% or more and 0.15% or less.
Cr contributes to an increase in the strength of a hot-rolled steel sheet by forming carbides. It is preferable that the Cr content be 0.005% or more to realize such an effect. On the other hand, when the Cr content is more than 0.2%, there is concern that there may be a decrease in the corrosion resistance of a hot-rolled steel sheet. Therefore, it is preferable that the Cr content be 0.005% or more and 0.2% or less, or more preferably 0.01% or more and 0.15% or less.
Mo contributes to an increase in the hole expansion formability and strength of a hot-rolled steel sheet by promoting formation of a bainite phase through increasing hardenability. It is preferable that the Mo content be 0.005% or more to realize such effects. However, when the Mo content is more than 0.2%, since a martensite phase tends to be formed, there is a possibility that there may be a deterioration in the bending workability of a hot-rolled steel sheet. Therefore, it is preferable that the Mo content be 0.005% or more and 0.2% or less, or more preferably 0.01% or more and 0.15% or less.
In addition, the hot-rolled steel sheet may contain, as needed, at least one selected from the group consisting of Ca: 0.0002% or more and 0.01% or less and REM: 0.0002% or more and 0.01% or less.
Since Ca is a chemical element which controls the shape of sulfide inclusions, Ca is effective in increasing the bending workability of a hot-rolled steel sheet. It is preferable that the Ca content be 0.0002% or more to realize such an effect. However, when the Ca content is more than 0.01%, there is a possibility that surface defects may occur in a hot-rolled steel sheet. Therefore, it is preferable that the Ca content be 0.0002% or more and 0.01% or less, or more preferably 0.0004% or more and 0.005% or less.
Since REM, like Ca, controls the shape of sulfide inclusions, REM reduces the negative effect of sulfide inclusions on the bending workability of a hot-rolled steel sheet. It is preferable that REM content be 0.0002% or more to realize such an effect. However, when REM content is more than 0.01%, since there is a decrease in the cleanness of steel, there is a tendency for the hole expansion formability of a hot-rolled steel sheet to decrease. Therefore, when REM is added, it is preferable that REM content be 0.0002% or more and 0.01% or less, or more preferably 0.0004% or more and 0.005% or less.
The balance other than the chemical elements described above includes Fe and inevitable impurities. Examples of the inevitable impurities include Sb, Sn, and Zn. It is acceptable that the contents of Sb, Sn, and Zn be respectively 0.01% or less, 0.1% or less, and 0.01% or less.
Hereafter, the reasons for the limitations on the microstructure of the hot-rolled steel sheet will be described.
The microstructure of the hot-rolled steel sheet has a structure that a microstructure in the surface layers placed on the upper and lower surface sides of the steel sheet (hereinafter, called surface regions) and a microstructure in the inside of the steel sheet other than the surface regions (hereinafter, called inner region), where the microstructure in the inner region is interposed between the microstructures of the surface regions on the upper and lower surface sides of the steel sheet. While the microstructure in the inner region is controlled to be substantially a bainite single phase, the microstructures in the surface regions are controlled to include mainly a ferrite phase such that the microstructures in the surface regions are softer than that in the inner region to increase the bending workability of a hot-rolled steel sheet while keeping a high strength of 980 MPa or more in terms of tensile strength TS.
The microstructure in the surface regions is controlled to include mainly a ferrite phase in an amount of 80% or more in terms of area fraction and the balance being at least one selected from a bainite phase, a martensite phase, and a retained austenite phase in an amount of 0% or more and 20% or less in terms of area fraction.
When the area fraction of a ferrite phase, which is a main phase, in the surface regions is less than 80%, since there is a decrease in the bending workability of a hot-rolled steel sheet, it is difficult to achieve a tensile strength of 980 MPa or more and satisfactory bending workability. Therefore, the area fraction of a ferrite phase in the surface regions is 80% or more, preferably 90% or more, or it may be 100% (which means a ferrite single phase).
In the surface regions, microstructures other than a ferrite phase are at least one of a bainite phase, a martensite phase, and a retained austenite phase, and the total area fraction of these phases is 0% or more and 20% or less, or preferably 10% or less.
On the other hand, the microstructure of the inner region is controlled to include mainly a bainite phase in an amount of more than 90% in terms of area fraction and the balance being at least one selected from the group of a ferrite phase, a martensite phase, and a retained austenite phase in an amount of 0% or more and less than 10% in terms of area fraction.
Area fraction of a bainite phase in the inner region: more than 90%
When the area fraction of a bainite phase, which is a main phase, in the inner region is 90% or less, since there is a decrease in the strength and bending workability of a hot-rolled steel sheet, it is not possible to stably achieve the desired high strength and satisfactory bending workability. Therefore, the area fraction of a bainite phase in the inner region is more than 90%, preferably 95% or more, and most preferably 100% (which means a bainite single phase).
Total Area Fraction of a Ferrite Phase, a Martensite Phase, and a Retained Austenite Phase in the Inner Region: 0% or More and Less than 10%
In the inner region, microstructures other than a bainite phase are one or more of a ferrite phase, a martensite phase, and a retained austenite phase, and the total area fraction of these phases is 0% or more and less than 10%, or preferably 5% or less.
The Proportions of the Surface Regions in the Thickness Direction of the Steel Sheet: 1.0% or More and 5.0% or Less of the Whole Thickness Respectively from the Upper and Lower Surfaces of the Steel Sheet
By controlling the proportions of the surface regions to the whole hot-rolled steel sheet to achieve a satisfactory strength-bending workability balance of the hot-rolled steel sheet, a hot-rolled steel sheet having a tensile strength of 980 MPa or more and being excellent in terms of bending workability is obtained. When the depths of the surface regions in the thickness direction of the steel sheet are less than 1.0% of the whole thickness respectively from the upper and lower surfaces of the steel sheet, it is difficult to provide a hot-rolled steel sheet with satisfactory bending workability, and a crack tends to occur when the hot-rolled steel sheet is subjected to bending work. On the other hand, when the depth of the soft surface regions, which increases bending workability, in the thickness direction of the steel sheet is more than 5.0% of the whole thickness respectively from the upper and lower surfaces of the steel sheet, since there is a decrease in the strength of the whole hot-rolled steel sheet, it is not possible to achieve the desired tensile strength of 980 MPa or more. Therefore, the proportions of the surface regions in the thickness direction of the steel sheet are 1.0% or more and 5.0% or less, or preferably 1.5% or more and 3.5% or less, of the whole thickness respectively from the upper and lower surfaces of the steel sheet.
As described above, by specifying a chemical composition and a microstructure, it is possible to obtain a high-strength hot-rolled steel sheet having a tensile strength TS of 980 MPa or more and bending workability which is required for materials for automotive parts. Although there is no particular limitation on the thickness of the hot-rolled steel sheet, it is preferable that the thickness be about 3.2 mm or more and 14 mm or less.
Hereafter, the preferable method of manufacturing the hot-rolled steel sheet will be described.
Our methods include heating a steel material having the chemical composition described above in a temperature range of 1250° C. or higher, then holding the heated steel material in the temperature range for 3600 seconds or more, performing hot rolling including rough rolling and finish rolling under the condition that the finish delivery temperature is 840° C. or higher and 940° C. or lower, starting cooling immediately after hot rolling has been finished, performing cooling at an average cooling rate of 25° C./s or more, and performing coiling at a coiling temperature of 350° C. or higher and 500° C. or lower. “° C.” represents a “surface temperature”, unless otherwise noted.
There is no particular limitation on what method is used to manufacture a steel material, and any of the common methods can be used to manufacture molten steel having the chemical composition described above, using a converter and the like, and forming a steel material such as a slab, using a casting method such as a continuous casting method. Also, an ingot casting and blooming method may be used.
The heating temperature of the steel material and the holding time of the steel material at the heating temperature are important factors in the manufacturing conditions. By heating a steel material such as a slab at a heating temperature of 1250° C. or higher, and by holding the heated steel material in the heating temperature range of 1250° C. or higher for 3600 seconds or more, since the surface layers of the steel material are decarburized, there is a decrease in the carbon concentration in the surface layers. As a result, since a ferrite phase is more likely to be formed in the surface regions of the steel material than in the inner region, it is possible to stably achieve the microstructure for a hot-rolled steel sheet described above.
In the steel material, almost all the carbonitride-forming elements such as Ti are present in the form of large-size carbonitrides. The presence of such large-size non-uniform carbonitrides causes a deterioration in the bending workability of a hot-rolled steel sheet. To make such large-size precipitates solid solutions formed before hot rolling process, it is necessary to limit the heating temperature of the steel material to 1250° C. or higher, or preferably 1260° C. or higher and 1350° C. or lower. In addition, the holding time of the steel material in a temperature range of 1250° C. or higher is 3600 seconds or more, or preferably 4000 seconds or more. However, when the holding time of the steel material in a temperature range of 1250° C. or higher is excessively long, since there is an increase in scale generation amount, for example, biting of scale tends to occur in the subsequent hot rolling process, which results in concern that there may be a deterioration in the surface quality of a hot-rolled steel sheet. Therefore, it is preferable that the holding time be 7200 seconds or less.
Following heating and holding the steel material, hot rolling including rough rolling and finish rolling is performed on the steel material. There is no particular limitation on what conditions are used for the rough rolling as long as a desired size for a sheet bar is achieved. Following the rough rolling, finish rolling is performed. It is preferable to perform descaling before finish rolling is performed or between the rolling stands in the middle of finish rolling.
The finish delivery temperature is one of the important factors in the manufacturing conditions. When the finish delivery temperature is lower than 840° C., since there is an increase in the area fraction of a ferrite phase when rolling is performed for forming a dual phase of a ferrite phase and an austenite phase, it is difficult to achieve the desired microstructure described above for a hot-rolled steel sheet. On the other hand, when the finish delivery temperature is excessively higher than 940° C., since there is an increase in hardenability due to the growth of austenite grains in the surface regions of the steel sheet, phases other than a ferrite phase such as a bainite phase tend to be formed, which makes it difficult to achieve the desired microstructure described above for a hot-rolled steel sheet. Therefore, the finish delivery temperature is 840° C. or higher and 940° C. or lower, preferably 850° C. or higher and 930° C. or lower, or more preferably 860° C. or higher and 920° C. or lower.
Immediately after finish rolling has been performed, preferably within 1.5 seconds, accelerated cooling is started, cooling is stopped at a coiling temperature and, then, the hot-rolled steel sheet is coiled in a coil shape. When the average cooling rate from the finish delivery temperature to the coiling temperature is less than 25° C./s, it is not possible to form sufficient amount of bainite phase in the inner region of a hot-rolled steel sheet. Therefore, the average cooling rate described above is 25° C./s or more, or preferably 30° C./s or more. Although there is no particular limitation on the upper limit of the average cooling rate, since it is difficult to achieve the desired microstructure in the surface regions due to bainite transformation being promoted when the average cooling rate is excessively large, it is preferable that the average cooling rate be 120° C./s or less. The average cooling rate described above is the average cooling rate in terms of the surface temperature of a steel sheet.
When the coiling temperature is lower than 350° C., a martensite phase and a retained austenite phase, which are hard, tend to be formed in the inner region of a hot-rolled steel sheet. As a result, since it is not possible to achieve the desired microstructure, it is difficult to provide a hot-rolled microstructure the desired bending workability. On the other hand, when the coiling temperature is higher than 500° C., since a ferrite phase tends to be formed in the inner region of a hot-rolled steel sheet, large-size pearlite phase and large-size martensite phase are formed, which results in a decrease in the strength and bending workability of a hot-rolled steel sheet. Considering the reasons described above, the coiling temperature is 350° C. or higher and 500° C. or lower, or preferably 350° C. or higher and 450° C. or lower.
To reduce segregation of the composition in steel at a continuous casting, for example, electromagnetic stirring (EMS) or light-reduction casting (IBSR) may be used. By performing an electromagnetic stirring treatment, since equiaxial crystals are formed in the central portion in the thickness direction in a steel sheet, it is possible to reduce the segregation. In addition, when light-reduction casting is performed, since the flow of molten steel in a non-solidified portion in a continuous cast slab is prevented, it is possible to reduce the segregation in the central portion in the thickness direction in a steel sheet. By using at least one of these treatments to reduce segregation, it is possible to further raise the level of bending workability described below.
After coiling has been performed, as with common methods of manufacturing a hot-rolled steel sheet, temper rolling may be performed, or scale formed on the surface of a steel sheet may be removed by performing pickling. Moreover, a plating treatment such as hot dip galvanizing or electrogalvanizing or chemical conversion coating may be performed.
Molten steels having the chemical compositions given in Table 1 were manufactured using a converter, and then slabs (steel materials) were manufactured using a continuous casting method. In hot-rolled steel sheets other than hot-rolled steel sheet No. 1′ composed of steel A given in Tables 1 through 3 described below, electromagnetic stirring (EMS) was performed to reduce the segregation of composition when continuous casting was performed. Subsequently, by heating and holding these steel materials under the conditions given in Table 2, by performing hot rolling including rough rolling and finish rolling under the conditions given in Table 2, by performing cooling under the conditions given in Table 2 after finish rolling had been performed, and by performing coiling at the coiling temperatures given in Table 2, hot-rolled steel sheets having the thicknesses given in Table 2 were manufactured.
Microstructure observation, a tensile test, and a bending test were performed on test pieces taken from the obtained hot-rolled steel sheets. Microstructure observation and the tests were performed using the following methods.
By taking a test piece for a scanning electron microscope (SEM) from the obtained hot-rolled steel sheet, by polishing a cross section in the thickness direction parallel to the rolling direction, by emergence of a microstructure using an etching solution (3%-nital solution), and by observing the vicinity of surface layers using a scanning electron microscope (SEM) at a magnification of 800 to 1500 times, surface regions were identified. Since a ferrite phase is observed more in surface regions than in an inner region, it is possible to distinguish surface regions from an inner region.
After the surface regions had been identified, by determining the depth of the region in which the surface region was formed on each of the upper and lower surface sides of the test piece (depth in the thickness direction from each of the upper and lower surfaces of the test piece), the proportion of the surface region which was formed on each of the upper and lower surfaces of the test piece in the thickness direction of the test piece (the thickness direction of the steel sheet) was determined. Specifically, by determining the depth d1 of the region in which the surface region was formed on the upper surface side of the test piece (depth in the thickness direction from the upper surface of the test piece) and the depth d2 of the region in which the surface region was formed on the lower surface side of the test piece (depth in the thickness direction from the lower surface of the test piece), by calculating the average value d (=(d1+d2)/2) of these depths, and by calculating the ratio (d/t×100(%)) of the average value d to the total thickness t of the test piece (that is, the thickness of the hot-rolled steel sheet), the proportion of the surface region which had been formed on each of the upper and lower surface sides in the thickness direction of the test piece (the thickness direction of the steel sheet) was determined. The depths (d1 and d2) described above were determined based on the scale bars in the images obtained using a SEM at a magnification of 800 to 1500 times.
The area fractions of the each constituent phases of the surface region were determined by taking photographs using a SEM at a magnification of 3000 times in 5 fields of view at the central position in the depth direction of the surface region and the vicinity of the central position and by performing image analysis within the range of ±20 μm in the depth direction from the central position to quantify the area fractions of the constituent phases. The area fractions of the constituent phases of the inner region were determined by taking photographs using a SEM (scanning electron microscope) at a magnification of 3000 times in 5 fields of view each at a position located at ¼ of the thickness and at a position located at ½ of the thickness and by performing image analysis to quantify the area fractions of the constituent phases.
A tensile test was performed in accordance with a method prescribed in JIS Z 2241 (2011) on a JIS No. 5 tensile test piece (having a GL of 50 mm) which had been taken from the obtained hot-rolled steel sheet so that the tensile direction was at a right angle to the rolling direction to obtain yield strength (yield point) YP, tensile strength TS, and total elongation El.
(iii) Bending Test
After performing shearing work on the obtained hot-rolled steel sheet, a bending test piece of 20 mm×150 mm was taken so that the longitudinal direction of the test piece was at a right angle to the rolling direction. A 180° bending test was performed on the test piece having a shear plane in accordance with a pressing bend method prescribed in JIS Z 2248 (2006). By performing the test on three test pieces for each case, by defining a limit bending radius R (mm) as the minimum bending radius with which a crack did not occur, and by calculating an R/t value by dividing R by the thickness t (mm) of the hot-rolled steel sheet, bending workability of the hot-rolled steel sheet was evaluated based on the R/t value. An R/t value of 0.50 or less was evaluated as a case of excellent bending workability.
Obtained results are given in Table 3.
C
0.07
F
0.2
I
4.0
K
0.20
L
0.05
970
C
1200
3000
800
10
F
14
520
15
I
18
K
19
L
0.5
61
C
53
79
83
10
F
0.3
33
14
53
77
81
15
I
0.7
36
18
K
82
85
19
L
The hot-rolled steel sheets of the examples were all hot-rolled steel sheets having the desired strength (980 MPa or more in terms of TS) and excellent bending workability (R/t value of 0.50 or less). On the other hand, in the hot-rolled steel sheets of the comparative examples, which were out of our range, the desired strength or satisfactory bending workability was not achieved.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2013-084449 | Apr 2013 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2014/001380 | 3/11/2014 | WO | 00 |
