JP6293997B2 - High-strength steel sheet with excellent stretch flangeability and bending workability, and method for producing molten steel for the steel sheet - Google Patents

Description

  The present invention relates to a high-strength steel sheet suitable for use in undercarriage parts of transportation equipment and a method for melting the molten steel, and in particular, a high-strength steel sheet excellent in stretch flangeability and bending workability and the melting of the molten steel. It is about the method.

There is an increasing demand for high strength and light weight hot-rolled steel sheets for automobiles from the viewpoint of improving the safety of automobiles and improving fuel efficiency leading to environmental conservation.
Among the parts for automobiles, the mass of frames and arms, especially called undercarriage systems, occupies a large proportion of the mass of the entire vehicle body, so by reducing the thickness by increasing the strength of the materials used for these parts It becomes possible to realize the weight reduction.
Further, the material used for the undercarriage system is frequently used for press forming, and high bending workability is required from the viewpoint of preventing cracking during press forming, and high strength steel sheets are widely used. Among these, hot rolled steel sheets are mainly used because of price advantages. In addition, cold-rolled steel sheets and galvanized steel sheets are used for the purpose of reducing the thickness by using high-strength steel sheets for reinforcing materials and under-floor members, especially small bending members such as seat slide rails. Is mainly used.

Among them, high strength, good workability, and good formability can be achieved by combining a low yield ratio DP steel plate that combines a ferrite phase and a martensite phase, or a composite of a ferrite phase and a (residual) austenite phase. TRIP steel sheets are known.
However, although these steel plates are excellent in high strength, workability and ductility, they cannot be said to have excellent hole expandability, that is, stretch flangeability and bending workability. Stretch flanges such as suspension parts In structural parts that require formability, bainite-based steel sheets are generally used, although the ductility is somewhat inferior.

  One of the reasons why a composite steel sheet such as a ferrite phase and martensite phase composite steel sheet (hereinafter sometimes referred to as “DP steel sheet”) is inferior in stretch flangeability is a soft ferrite phase and hard martensite. It is considered that because it is a composite of the site phase, stress concentrates at the boundary between both phases during hole expansion processing, and it cannot follow deformation and tends to be a starting point of fracture.

Further, when these steel pieces are heated in a heating furnace or rolled, an oxide scale is formed on the surface. This oxide scale needs to be hot-rolled or descaled before processing (deske, oxide scale removal), but at the time of descaling, if the scale cannot be removed sufficiently and remains on the surface of the steel plate, Hot rolling or biting the scale during processing may cause wrinkles in the product or red scale.
The wrinkles that are bitten by these scales, red scales, etc. cause problems by causing deterioration of the surface properties, plating adhesion, and plating adhesion of the product steel plate, and removing wrinkles for the purpose of avoiding problems. Cost is increased to increase the number of processes.

Among steel sheets that achieve both high strength, good workability and good formability, the deterioration of surface properties, plating adhesion, and plating adhesion of the product steel sheet produced by wrinkles and red scales that bite these scales. A material that is strict in deterioration or the like is a component system in which Si is not added because it does not generate the scale component Fe ₂ SiO ₄ which is one of these causes. However, depending on the dew point condition of the heating furnace and the rolling condition, Etc. may occur.

In addition, since these component systems to which Si is not added are free of Si, which is an important deoxidizing element of molten steel, the oxygen potential is relatively high, and there are many Al ₂ O ₃ oxide inclusions. There are also surface defects and internal defects in the system, and there are also problems in melting such as difficulty in removing molten steel due to high oxygen potential.
Furthermore, since the Si element necessary for increasing the strength is not added, it is necessary to increase the amount of Mn to increase the strength or increase other precipitation strengthening elements. Workability and formability are inferior to those of other materials.

  First, in order to overcome the problems of wrinkles, surface properties, and plating adhesion, it is difficult to apply when the Si concentration exceeds 0.1%, but the Si concentration is reduced to 0.1% or less. A method of controlling the atmosphere of the heating furnace and the slab heating temperature has been proposed based on the steel. For example, in Patent Document 1, when an ordinary steel slab having a Si concentration before hot rolling of 0.1% or less is heated in a heating furnace, an atmosphere having an air ratio of 1.0 to 1.2 and a slab heating temperature are set. The method characterized by heating within the range of 1050 to 1250 degreeC is disclosed.

  Further, as a technique from the viewpoint of the adhesion of the scale after hot rolling and the peelability of the scale in mechanical descaling before the secondary processing, for example, Patent Document 2 discloses that the steel material after hot rolling is steam or mist. A technique is disclosed in which the surface is oxidized by passing it through water, and the temperature of the oxidation treatment is controlled to form firelite at the interface between the scale and the ground iron.

Patent Document 3 discloses a technology for obtaining a hot-dip galvanized steel sheet having high strength and excellent hole expansibility by forming carbide, nitride, carbonitride with a high concentration of Ti and Nb in a Si-less component system. Is disclosed.
Furthermore, in Patent Document 4, almost no Al is added, and a large amount of dissolved oxygen is left, so that almost no inclusions are generated in the molten steel, and a steel sheet having excellent surface properties is formed. Cu, Nb, A technique for obtaining a steel sheet having high strength and excellent workability and formability by adding B is disclosed.

Japanese Patent Application Laid-Open No. 2004-10954 JP 2008-49391 A JP 2011-241429 A JP 2006-257542 A

  By the way, the method for preventing defects such as linear scale defects and plating unevenness by controlling the atmosphere of the heating furnace and the slab heating temperature as disclosed in the above-mentioned Patent Document 1 is surely a good product with high surface quality. Although it can be obtained, significant improvement in stretch flangeability and bending workability has not been confirmed. The same is true of the manufacturing method from the viewpoint of scale peelability as disclosed in Patent Document 2, and no significant improvement in stretch flangeability and bending workability has been confirmed.

And, as disclosed in Patent Document 3, it is a Si-less component system, and by forming Ti, Nb at a high concentration and forming carbide, nitride, carbonitride, it has high strength and excellent hole expansibility. Although the technique for obtaining a hot-dip galvanized steel sheet suppresses the formation of hard structures such as coarse cementite and martensite having a high C concentration and exhibits excellent hole expansibility, no significant improvement in bending workability has been confirmed. In addition, the generation of cracks cannot be prevented when severe hole enlargement processing is performed only by suppressing the formation of coarse carbides.
Further, since a large amount of Mn and S are contained in a predetermined amount, according to the experimental knowledge of the present inventors, it is considered that coarse MnS inclusions are generated. It is not sufficient to prevent the occurrence of cracks when severe hole enlargement processing is performed only by reducing the amount of carbide formation.

Further, as disclosed in Patent Document 4, almost no Al is added and a large amount of dissolved oxygen is left, so that almost no inclusions are formed in the molten steel, and a steel sheet having excellent surface properties is made, Cu and Nb A high-strength steel plate in which Y and B are dispersed in the steel plate exhibits excellent surface properties, but no significant improvement in stretch flangeability and bending workability has been confirmed.
And, in the smelting stage in steelmaking, since desulfurization treatment under the condition that relatively high free oxygen exists is used substantially without Al, it is difficult to desulfurize even to extremely low sulfur. Since a predetermined amount of Mn and S are contained, it is considered that coarse MnS inclusions are produced. Therefore, severe hole expansion is required only by reducing the amount of coarse oxide inclusions produced. When processing is performed, it is not sufficient to prevent the occurrence of cracks.

  According to the studies by the present inventors, it has been found that the cause of the problems described in Patent Documents 1, 2, 3, and 4 is the presence of elongated sulfide inclusions mainly composed of MnS in the steel sheet. . In addition, when soluble Ti is increased at the same time, it partially combines with coarse TiS and MnS to become (Mn, Ti) S, and the presence of (Mn, Ti) S that stretches similarly to MnS has an adverse effect. I understood. That is, when the steel sheet is repeatedly deformed, internal defects are generated around the extended coarse MnS inclusions on the surface layer or in the vicinity thereof, and propagated as cracks. Since it tends to be the starting point of occurrence, it becomes a factor that the stretch flangeability and bending workability are lowered.

  In other words, the existence of sulfide inclusions mainly composed of MnS described in Patent Documents 1, 2, 3, and 4 will be described in detail. Mn is an element that contributes effectively to increase the strength of materials together with C and Si. Therefore, in a high-strength steel sheet, it is common to set the concentration of Mn high in order to ensure strength. Furthermore, in the processing of a normal steelmaking process, S is also included in an amount of about 5 to 150 ppm. Normally, MnS is present in the ingot (slab).

These MnS inclusions are easily deformed when the ingot is hot-rolled and cold-rolled, so that they become stretched coarse MnS-based inclusions, which are bending workability and stretch flangeability (hole expansion workability). It will cause the decrease.
However, until now, among steel sheets that achieve both high strength, good workability and good formability, surface texture deterioration, plating adhesion, Applying to strict materials for deterioration of plating adhesion, etc., while actively improving the suppression of scale flaws and plating adhesion, stretch flangeability and bending from the viewpoint of precipitation and deformation control of MnS inclusions There is no example that suggests a high-strength steel sheet excellent in workability and a method for producing molten steel for the steel sheet.

Therefore, the present invention has been devised in view of the above-mentioned problems, and the object of the present invention is to perform complex deoxidation of the molten steel at the steel making stage and to obtain coarse Al ₂ O in the ingot. ₃ based oxide, not produce MnS-based inclusions, oxides and fine complex precipitates or as inclusions in the form a oxysulfide, without being further deformed during the rolling, the starting point and becomes hard fine spherical inclusions cracking As a high strength steel sheet with improved stretch flangeability and bending workability while suppressing the generation of wrinkles and red scale on the steel slab and the steel sheet surface. It is to provide a manufacturing method.

  In order to solve the above-mentioned problems, the present inventors have performed complex deoxidation by adding Al, Ti, Ce, La, Nd, Pr, and Ca, and intervening fine MnS in the ingot (slab). The concentration of hydrogen ions at the interface that precipitates and disperses in the steel sheet as fine spherical inclusions that do not undergo deformation during rolling and are unlikely to start cracking, and that affect the corrosion of the steel slab and steel sheet surface. We focused on elucidating methods to improve stretch flangeability and bending workability by obtaining the effect of suppressing wrinkle generation and red scale generation while suppressing the rise of steel.

  As a result, fine and hard Ce oxide, La oxide, Nd oxide, Pr oxide, cerium oxysulfide, lanthanum oxysulfide, neodymium oxysulfide produced by deoxidation by addition of Ce, La, Nd, and Pr In addition, it forms prasedioxide and is further combined with added Ca to contain one or more of Ce, La, Nd, Pr, Al, Ti, Ca, and O, S An inclusion phase containing one or two of the above, an inclusion phase containing one or more of Ce, La, Nd, Pr, Ti, Mn, and containing Ca, S, and Ti There is an inclusion phase containing one or more of Mn and S, and one or more inclusion phases of three inclusion phases have a circle equivalent diameter of 0.5 to 5 μm. One of the combined When the inclusions are formed, deformation of the precipitated MnS inclusions is difficult to occur even during rolling. Therefore, the stretched coarse MnS inclusions are remarkably reduced in the steel sheet, and during repeated deformation or hole expansion processing, At the time of bending, it was found that the MnS-based inclusions are less likely to become crack initiation points and crack propagation paths, which leads to improvements in hole expansibility and the like.

In addition to making the precipitate a fine oxide or MnS inclusion, (Ce + La + Nd + Pr) / T. O> 0.5, and Ca / T. By setting O> 0.6, the oxygen potential in the molten steel can be reduced without adding Si, and desulfurization can proceed relatively easily to extremely low S under this low oxygen potential. It has been found that a finer MnS inclusion can be obtained and the remaining sulfur content can be reliably fixed to a fine and hard inclusion. Furthermore, if this component ratio can be achieved, there is no coarse Al ₂ O ₃ -based oxide, surface flaws caused by the Al ₂ O ₃ -based oxide can be suppressed, and the corrosion of steel slabs and steel sheet surfaces is affected. In addition to improving the stretch flangeability and bending workability while suppressing an increase in the hydrogen ion concentration at the interface, it has been found that it can dramatically improve the generation of scale wrinkles and red scale. The present invention has been completed.
It was observed that TiN and TiC were precipitated together with MnS inclusions on fine and hard Ce oxide, La oxide, cerium oxysulfide, and lanthanum oxysulfide, but bending workability and elongation were also observed. Since it has been confirmed that there is almost no influence on the flange property, TiN and TiC are not targets of MnS inclusions.
It was also found that by adding Ti to increase acid-soluble Ti in the steel, the crystal grains can be refined by the effect of pinning solid solution Ti or Ti carbonitride. Accordingly, it was found that the MnS inclusions in the steel can be made into a fine spheroid without stretching as much as possible, and the crystal grains can be made fine at the same time, so that both stretch flangeability and bending workability can be achieved.

  The gist of the high strength steel sheet excellent in stretch flangeability and bending workability according to the present invention and the method for producing molten steel for the steel sheet is as follows.

(1) In mass%,
C: 0.03-0.25%,
Si: 0.001 to 0.02%,
Mn: 0.5 to 3.0%
P: 0.05% or less,
T.A. O: 0.0050% or less,
S: 0.0001 to 0.008%,
N: 0.0005 to 0.01%,
Acid-soluble Al: 0.01 to 1.3%
Acid-soluble Ti: 0.008 to 0.20%
Ca: 0.0005 to 0.0050%,
Total of one or more of Ce, La, Nd and Pr: 0.001 to 0.01%,
Further, on a mass basis, (Ce + La + Nd + Pr) / T. O> 0.5, and Ca / T. O> 0.6
The balance is a steel plate of chemical composition consisting of iron and inevitable impurities,
The steel sheet contains one or more of Ce, La, Nd, Pr, Al, Ti, Ca, and an inclusion phase containing one or two of O, S, and
An inclusion phase containing one or more of Ce, La, Nd, Pr, Ti, Mn, and containing Ca, S;
There is an inclusion phase containing one or more of Ti, Mn, S,
Of the three inclusion phases, one or more inclusion phases are combined, and the fine and hard Ce oxide, La oxide, Nd oxide, Pr oxide, and cerium oxy occupy most of the inclusion phase. A composite inclusion in which sulfide, lanthanum oxysulfide, neodymium oxysulfide, praseodymium oxysulfide and Ca oxide or Ca oxysulfide are compositely precipitated, and further MnS inclusions are precipitated, and the equivalent circle diameter is 0.5 to 5 μm. It forms a size one spherical composite inclusions state, and are more than 30% of the total inclusions number of the spherical composite inclusions number proportion the size of the circle equivalent diameter 0.5~5μm of the spherical For inclusions having a circle equivalent diameter of 1 μm or more of the composite inclusion, the ratio of the number of inclusions having a major axis / minor axis of 3 or less is 50% or more of the total number of inclusions having a circle equivalent diameter of 1 μm or more, Luo, the major axis / minor axis is contained in the 3 following inclusions, Ce, La, Nd, 0.5 to 95% by mass Rukoto one or more total the average composition of the Pr High strength steel sheet with excellent stretch flangeability and bending workability.

( 2 ) The high-strength steel sheet excellent in stretch flangeability and bending workability according to ( 1), wherein an average grain size of crystals in the structure of the steel sheet is 10 μm or less.

( 3 ) Furthermore, in mass%,
Nb: 0.001 to 0.10%,
V: 0.01-0.10%
The high strength steel plate excellent in stretch flangeability and bending workability as described in (1) or ( 2) characterized by containing any 1 type or 2 types.

( 4 ) Furthermore, in mass%,
Cu: 0.1 to 2%,
Ni: 0.05 to 1%,
Cr: 0.01-1%,
Mo: 0.01 to 0.4%,
B: 0.0003 to 0.005%
The high strength steel sheet excellent in stretch flangeability and bending workability according to any one of (1) to ( 3 ), characterized by containing any one or more of the above.

( 5 ) Furthermore, in mass%,
Zr: 0.001 to 0.01%
A high-strength steel sheet excellent in stretch flangeability and bending workability as described in any one of (1) to ( 4 ).

( 6 ) In the refining process in steelmaking, C is 0.03 to 0.25% and Si is not added to the molten steel processed in mass%, P is 0.05% or less, and S is 0.0001% or more. , Mn is added or adjusted to 1.0 to 3.0% and N is 0.0005 to 0.01%, and then Al is 0.01% or more of acid-soluble Al. O is added so that it becomes 0.0050% or less, and then Ti is added so that it becomes 0.008% or more as acid-soluble Ti, and then, one or two of Ce, La, Nd, Pr More seeds were added, and on a mass basis, (Ce + La + Nd + Pr) / T. After the total of one or more of O> 0.5, Ce, La, Nd, and Pr is 0.001 to 0.01%, Ca is added, and further, on a mass basis, Ca / T . O> 0.6, Ca: 0.0005-0.0050% is added or adjusted so that it is excellent in stretch flangeability and bending workability as described in (1) or ( 2) A method for producing molten steel for high-strength steel sheets.

( 7 ) In the refining step, after deoxidizing with Al and adding Ti, before adding one or more of Ce, La, Nd, and Pr, Nb is further added in an amount of 0.1% by mass. The stretch flangeability and bending workability described in ( 6 ) are characterized by adding 001 to 0.10% and V to be any one or two of 0.01 to 0.10%. An excellent method for producing molten steel for high-strength steel sheets.

( 8 ) In the refining step, after deoxidizing with Al and adding Ti, before adding one or more of Ce, La, Nd, and Pr, Cu is further added by 0.1% by mass. 1-2%, Ni 0.05-1%, Cr 0.01-1%, Mo 0.01-0.4%, B 0.0003-0.005% The method for melting molten steel for high-strength steel sheets excellent in stretch flangeability and bending workability as described in ( 6 ) or ( 7 ), wherein two or more types are added.

( 9 ) In the refining step, after deoxidizing with Al and adding Ti, before adding one or more of Ce, La, Nd, and Pr, Zr is further reduced to 0. The method for melting molten steel for high-strength steel sheets excellent in stretch flangeability and bending workability according to any one of ( 6 ) to ( 8 ), characterized by being added so as to be 001 to 0.01% .

  Incidentally, the high-strength steel plate in the present invention is a normal hot-rolled steel plate or cold-rolled steel plate, and includes use as it is as it is, or use after being subjected to surface treatment such as plating or painting.

  In the high-strength steel sheet having the above-described structure and excellent in stretch flangeability and bending workability, the adjustment of the composition of the molten steel is stabilized by Al deoxidation, and the formation of coarse alumina inclusions is suppressed. In the steel plate as fine spherical inclusions that are not deformed during rolling and are unlikely to start cracking because they are precipitated as inclusions in the form of fine composite precipitated oxide or oxysulfide in the ingot. In addition, the crystal grain size of the structure can be made fine, and stretch flangeability and bending workability can be improved.

  Further, in the method for producing molten steel of a high strength steel sheet excellent in stretch flangeability and bending workability according to the present invention, it is possible to produce coarse alumina inclusions while stabilizing component adjustment of the molten steel by Al deoxidation. It can be suppressed and deposited as a complex inclusion that is a fine composite precipitated oxide or oxysulfide in the ingot, so that it does not undergo deformation during rolling and is difficult to start cracking in the steel plate as a fine spherical inclusion It can be dispersed, the crystal grain size of the structure can be made fine, and a high-strength hot-rolled steel sheet excellent in stretch flangeability and bending workability can be obtained.

  Hereinafter, as a form for carrying out the present invention, a high-strength steel sheet excellent in stretch flangeability and bending workability will be described in detail. Hereinafter, the mass% in the composition is simply described as%.

  First, the experiment that led to the completion of the present invention will be described. The present inventor contains C: 0.06%, no addition of Si, Mn: 1.4%, P: 0.01% or less, S: 0.005%, N: 0.003%, with the balance being Fe The ingot was deoxidized with various elements to produce a steel ingot. The obtained steel ingot was hot-rolled to obtain a hot-rolled steel sheet having a thickness of 3 mm. These manufactured hot-rolled steel sheets were subjected to a tensile test, a hole expansion test, and a bending test, and the number density, form, and average composition of inclusions in the steel sheets were investigated.

First, in a hot rolled steel sheet manufactured by adding Al to molten steel and deoxidizing, Al ₂ O ₃ inclusions are present in the steel ingot, its melting point is as high as 2040 ° C., and it is not stretched during rolling. It exists in an angular shape. For this reason, it becomes a starting point of the crack of a steel plate at the time of a hole expansion process, and causes a decrease in bending workability and stretch flangeability (hole expansion processability). In addition, the MnS inclusions coarsely precipitated as inclusions in the steel ingot have a melting point as low as about 1610 ° C., and are easily stretched during rolling to become elongated MnS inclusions. Become.

Further, in a hot rolled steel sheet manufactured by adding Ca after deoxidation with Al, Ca melts and becomes larger due to interfacial energy, and CaOAl ₂ O ₃ inclusions and CaS (Fe, Mn) are contained in the ingot. , Al ₂ O ₃ ) -based inclusions are coarsely precipitated. Since these inclusions have a melting point of about 1390 ° C., they are easily stretched at the time of rolling and exist as stretched inclusions of about 50 to 100 μm, and lower bending workability and stretch flangeability (hole expansion workability). Cause.

Therefore, the present inventors deoxidized the molten steel with Al and stirred for about 2 minutes, and then added Ti, and thereafter, one, two, three, or four of Ce, La, Nd, and Pr. Stretch flangeability and bending workability were investigated for steel plates manufactured by adding and deoxidizing. As a result, it was confirmed that such a steel sheet can improve stretch flangeability and bending workability. Note that one or more of Ce, La, Nd, and Pr may be described as (Ce, La, Nd, and Pr) below.
The reason is that fine and hard Ce oxide, La oxide, Nd oxide, Pr oxide, cerium oxysulfide, lanthanum oxysulfide produced by deoxidation by addition of (Ce, La, Nd, Pr), MnS-based inclusions such as MnS and TiS are deposited on neodymium oxysulfide and prasedymium oxysulfide, and it is possible to suppress deformation of inclusions that are complex-precipitated oxides or oxysulfides during rolling. This is because the stretched coarse MnS inclusions can be remarkably reduced in the steel sheet.

  The reason why Ce oxide, La oxide, Nd oxide, Pr oxide, cerium oxysulfide, lanthanum oxysulfide, neodymium oxysulfide, and prasedium oxysulfide are miniaturized is that the interfacial energy between these and molten steel is low. It is because the aggregation and coalescence after the generation is also suppressed because it is low.

  The inventors subsequently added Ti while deoxidizing Al, deoxidized while changing the composition of Ce, La, Nd, and Pr, and then added Ca to produce a steel ingot. The obtained steel ingot was hot-rolled to obtain a hot-rolled steel sheet having a thickness of 3 mm. These manufactured hot-rolled steel sheets were subjected to a hole expansion test and a bending test, and the inclusion number density, form and average composition in the steel sheets were investigated.

Through such experiments, deoxidation was performed with Al in Si-free molten steel, Ti was added, and then one, two, three, or four of Ce, La, Nd, and Pr were added for deoxidation. After that, in the molten steel obtained by adding Ca and performing composite deoxidation, (Ce + La + Nd + Pr) / T. O> 0.5, and Ca / T. When O> 0.6 was obtained, a result that the oxygen potential in the molten steel suddenly decreased was obtained.
The above effects in the Si-free molten steel can be obtained even if the Si-added steel, ie, Al, Si, Ti, (Ce, La, Nd, Pr), Ca does not reach the combined deoxidation effect. Among the systems that have been deoxidized with various deoxidizing elements in the additive molten steel, the effect of lowering the oxygen potential was obtained most.

Because of the combined deoxidation effect, the Al ₂ O ₃ activity can be made extremely low, and it has been found that a steel sheet having excellent stretch flangeability and bending workability can be obtained as in the case of Si-added steel. Moreover, if this component ratio can be achieved, coarse Al ₂ O ₃ -based oxides can be eliminated, surface defects caused by Al ₂ O ₃ -based oxides can be suppressed, and generation of scale defects, red scale, etc. The result which was effective in generation | occurrence | production suppression was obtained.

The reason is considered as follows.
By adding Al to the molten steel, Al ₂ O ₃ inclusions are generated, some Al ₂ O ₃ inclusions are levitated and removed, and the remaining Al ₂ O ₃ inclusions remain in the molten steel. . Thereafter, by adding Ti and further adding (Ce, La, Nd, Pr), the Al ₂ O ₃ inclusions are reduced and decomposed, and fine and spherical Ce oxide, La oxide, Nd oxide, Pr REM oxysulfides such as oxides, cerium oxysulfides, lanthanum oxysulfides, neodymium oxysulfides, prasedimoxysulfides and the like are formed. Further, by adding Ca, the oxide and / or oxysulfide is equivalent to a fine and hard circle in a form in which inclusions containing (Ce, La, Nd, Pr), MnCa sulfide and the like are complex-precipitated. A composite inclusion having a diameter of 0.5 to 5 μm is formed.

  That is, the inclusion phase contains [1] one or more of Ce, La, Nd, Pr, Al, Ti, and Ca and one or two of O and S. A physical phase, and [2] inclusion phase containing one or more of Ce, La, Nd, Pr, Ti, Mn, and containing Ca, S, and [3] Ti, Mn, S There are three inclusion phases of inclusion phases containing one or more of the above, and a composite inclusion in which one or more inclusion phases among them are combined, for example, the following complex inclusion Form things.

Al—O—Ce—La—Nd—Pr—O—S—Ca inclusion phase [eg, Al ₂ O ₃ (Ce, La, Nd, Pr) ₂ O ₂ SCa], Ce—La—Nd—Pr A spherical composite inclusion in which an Mn—Ca inclusion phase [for example, (Ce, La, Nd, Pr) CaMnS] is combined into one inclusion,
Ca—Ti—S—Ce—La—Nd—Pr inclusion phase [eg, CaTiS (Ce, La, Nd, Pr)] and Ce—La—Nd—Pr—O—S—Ti—Ca inclusion phase [For example, (Ce, La, Nd, Pr) ₂ O ₂ STiCa] composite inclusions,
Ce—La—Nd—Pr—O—S—Al—O inclusion phase [eg, (Ce, La, Nd, Pr) ₂ O ₂ SAl ₂ O ₃ ] to Ti—Mn—Ca—S inclusion phase [For example, a spherical composite inclusion in which CaTiMnS] is combined into one inclusion.

  These compound inclusions are mainly oxysulfide (Ce, La, Nd, Pr) and are almost spherical, so once added metals such as Ce, La, Nd, Pr etc. melt and react. After forming a large number of very fine nuclei when forming oxysulfide, it was possible to phase-separate after that, or when some additional low-melting phase was added when Ca was further added, It is thought that these phases were fused.

These fine spheroidized composite inclusions have a high melting point of about 2000 ° C., and are not stretched by hot rolling, and show a finely spheroidized form in the hot-rolled steel sheet. Therefore, by forming spherical composite inclusions (REM oxysulfide composite inclusions) in the form of oxides or oxysulfides that have been compositely precipitated in this way, bending workability and stretch flangeability (hole expansion workability) are reduced. Can prevent the cause.
In addition, even if Ca is added before the addition of (Ce, La, Nd, Pr), Ca is a low melting point metal, and a Ca (O) -Al ₂ O ₃ based low melting point oxide is formed. Therefore, a hard and fine spherical composite compound cannot be obtained.

  Therefore, in the component system without addition of Si, in the combined deoxidation in the order of addition of Al, Ti, (Ce, La, Nd, Pr) and Ca, (Ce + La + Nd + Pr) / T. O> 0.5, and Ca / T. By appropriately performing the deoxidation method so as to obtain O> 0.6, the oxygen potential in the molten steel can be drastically reduced, and the above-described composite having an equivalent circle diameter of 0.5 to 5 μm Rolled spherical inclusions can be formed, and the number ratio of the composite spherical inclusions can be 30% or more of the total number of inclusions having a circle equivalent diameter of 0.5 to 5 μm. In some cases, the deformation of the complex-precipitated inclusion can be suppressed.

Therefore, in addition to obtaining the effect that the stretch flangeability and bending workability can be improved by significantly reducing the stretched coarse MnS inclusions in the steel sheet, the Al ₂ O ₃ oxide is also obtained. by capable of heterogeneous nucleation on a part of the hard composite inclusions, it is possible to reduce sharply the activity of Al ₂ O _3, since the coarse Al ₂ O ₃ based oxide is eliminated, Al ₂ Surface flaws caused by the O ₃ oxide can be suppressed.
In addition, it can suppress the increase of hydrogen ion concentration at the interface, which affects the corrosion of the low oxygen potential steel slab and steel sheet surface, dramatically reducing the occurrence of scale flaws and red scales. It was found that an effect can be obtained in prevention.

Based on the knowledge obtained from these experimental studies, the present inventors have studied the chemical composition conditions of the steel sheet and completed the present invention by designing the composition of the steel sheet, as will be described below. It was.
Hereinafter, the reason for limiting the chemical components of the high-strength steel sheet excellent in stretch flangeability and bending workability in the present invention will be described.

(C: 0.03-0.25%)
C is the most basic element that controls the hardenability and strength of steel, and contributes to the improvement of strength by increasing the hardness and depth of the hardened hardened layer. That is, this C is an essential element for securing the strength of the steel sheet, and at least 0.03% is required to obtain a high-strength steel sheet. However, if this C is excessively contained and exceeds 0.25%, workability and weldability deteriorate. In order to achieve the required strength and ensure workability and weldability, the C concentration is set to 0.25% or less in the present invention. Preferably it is 0.03 to 0.20%.

(Si: 0.001 to 0.07%)
When the content of Si exceeds 0.07%, scale formation in the hot rolling process is remarkable, leading to generation of wrinkles, causing deterioration of surface properties from the occurrence of red scale, etc., and plating adhesion and adhesion. Significantly deteriorates, and corrosion resistance deteriorates. For this reason, the upper limit of the Si concentration is set to 0.07%. In the claims, the upper limit of the Si concentration was set to 0.02% based on the example.
On the other hand, even if Si is not added, Si is picked up as a component of various alloy irons and reduction of SiO2 in the slag, so the Si content is less than 0.001%. Such extremely low Si causes an increase in manufacturing cost, and accordingly the lower limit is set to 0.001%.

(Mn: 0.5-3.0%)
Mn is an element useful for deoxidation in the steelmaking stage, and is an element effective for increasing the strength of the steel sheet together with C and Si. In order to obtain such an effect, it is necessary to contain 0.5% or more of this Mn. However, when Mn is contained in an amount exceeding 3.0%, ductility is lowered due to segregation of Mn and increase in solid solution strengthening. Further, since the weldability and the base metal toughness are also deteriorated, the upper limit of Mn is set to 3.0%. Preferably it is 1.0 to 2.6%.

(P: 0.05% or less)
P is an element inevitably contained, and is effective in that it acts as a substitutional solid solution strengthening element smaller than Fe atoms. However, if this P concentration exceeds 0.05%, it segregates at the grain boundaries of austenite and lowers the grain boundary strength, thereby lowering the torsional strength and causing deterioration of workability. The upper limit is 0.05%. Further, if solid solution strengthening is not necessary, it is not necessary to add P, and the lower limit value of P includes 0%.

(T.O: 0.0050% or less)
T.A. O forms an oxide as an impurity. T.A. When O is too high, mainly Al ₂ O ₃ inclusions increase, the oxygen potential of the system cannot be minimized, the toughness becomes extremely poor, and the surface flaws increase, so bending workability is rejected. Deteriorate. Therefore, in the present invention, T.I. The upper limit of O was 0.0050%.

(S: 0.0001 to 0.008%)
S is segregated as an impurity, and S combines with Mn to form a MnS-based coarse stretch inclusion to deteriorate stretch flangeability. Therefore, it is desirable that the concentration be as low as possible. On the other hand, even at a relatively high S concentration of about 0.008%, the MnS-based coarse stretched inclusions of the present invention are not subjected to desulfurization load in the secondary refining by the form control, without desulfurization cost, More material than the cost can be obtained. Therefore, the range of the S concentration in the present invention is set to a range from 0.0001% to 0.008% from a very low S concentration assuming desulfurization in secondary refining to a relatively high S concentration.

In the present invention, fine inclusions such as hard and hard Ce oxide, La oxide, Nd oxide, Pr oxide, cerium oxysulfide, lanthanum oxysulfide, neodymium oxysulfide, praseodymium oxysulfide and Ca oxide are included. above, is out analysis of MnS-based inclusions, by morphology control of MnS-based inclusions, deformation hardly occur during rolling, because it prevents the stretched inclusions, the upper limit of the concentration of S is described later As described above, it is defined in relation to the total amount of one or more of Ce, La, Nd, and Pr. Furthermore, when it exceeds 0.008%, cerium oxysulfide and lanthanum oxysulfide grow and become a size exceeding 5 μm, and when it becomes coarse, the toughness becomes extremely poor and the surface flaw increases. Therefore, the bending workability is worsened. For this reason, in this invention, the upper limit of S was made into 0.008%.

  That is, in the present invention, as described above, MnS is controlled in form by inclusions such as Ce oxide, La oxide, cerium oxysulfide, lanthanum oxysulfide, neodymium oxysulfide, praseodymium oxysulfide, and Ca oxide. Even if the concentration is relatively high within the range of 0.008% or less, it is possible to prevent adverse effects on the material by adding one or two of Ce or La in an amount corresponding thereto. That is, even if the concentration of S is high to some extent, by adjusting the addition amount of Ce or La or the like according to this, a substantial desulfurization effect can be obtained, and the same material as the ultra low sulfur steel can be obtained. In other words, it is possible to increase the degree of freedom for the upper limit by appropriately adjusting the S concentration with the total amount of Ce, La, Nd, and Pr. Therefore, in the present invention, there is no need to perform molten steel desulfurization in secondary refining to obtain ultra-low-sulfurized steel, which can be omitted, simplifying the manufacturing process, and reducing the desulfurization treatment cost associated therewith. It can be realized.

(N: 0.0005 to 0.01%)
N is an element that is inevitably mixed in steel because nitrogen in the air is taken in during the treatment of molten steel. N forms a nitride with Al or the like to promote the refinement of the base material structure. However, when the N content exceeds 0.01%, coarse precipitates such as Al are generated, and the stretch flangeability is deteriorated. For this reason, in the present invention, the upper limit of the concentration of N is set to 0.01%, preferably 0.005%. On the other hand, since it is expensive to make the concentration of N less than 0.0005%, 0.0005% is made the lower limit from the industrially feasible viewpoint.

(Acid-soluble Al: 0.01 to 1.3%)
In general, acid-soluble Al tends to become coarse due to clustering of its oxides, and if a large amount of coarse Al ₂ O ₃ is present, the toughness becomes extremely poor, surface defects increase, stretch flangeability, It is desirable to suppress as much as possible in order to degrade the bending workability. However, in the present invention, while performing Al deoxidation, (one or more of Ce, La, Nd, and Pr) and the combined and sequential deoxidation effect of Ca and coarse Al ₂ O ₃ and related to T. By setting the Ca concentration according to the O concentration (Ce, La, Nd, Pr concentration) and the Ca concentration, as described above, the Al ₂ O ₃ activity is kept low and the low oxygen potential is achieved while the Al content in the molten steel is reduced. ₂ O ₃ inclusions and clusters were divided to form fine inclusions, and a new region was found that does not lead to material deterioration or surface defects.

  For this reason, in the present invention, there is no need to provide a restriction that Al is not substantially added in order to avoid coarse clusters of alumina-based oxides as in the prior art, and the degree of freedom particularly with respect to the concentration of this acid-soluble Al. Can be increased. Moreover, by making the acid-soluble Al 0.01% or more positively, the oxygen potential in the steel is extremely low by using the combined deoxidation with Al, (Ce, La, Nd, Pr), and Ca. We can enjoy effect to suppress.

  Furthermore, the combined deoxidation effect by Al, (Ce, La, Nd, Pr), and Ca can suppress the increase of the hydrogen ion concentration at the interface, which affects the corrosion of the steel sheet surface. This is effective in preventing the occurrence of scale wrinkles and red scales. Corrosion resistance is also improved by the high Al concentration. It is preferable to set it as 1.3% or less from the surface of the raise of the effect, and the addition cost.

In addition, the acid-soluble Al concentration referred to here is a measurement of the concentration of Al dissolved in an acid, and is an analytical method utilizing the fact that dissolved Al dissolves in an acid and Al ₂ O ₃ does not dissolve in an acid. is there. Here, examples of the acid include a mixed acid mixed at a ratio (mass ratio) of hydrochloric acid 1, nitric acid 1, and water 2. By using such an acid, it can be separated into Al soluble in acid and Al ₂ O ₃ not soluble in acid, and the acid soluble Al concentration can be measured.

(Acid-soluble Ti: 0.008 to 0.20%)
Ti is one of the main deoxidizing elements, and forms carbides, nitrides, carbonitrides, and sufficiently heats before hot rolling to increase the number of nucleation sites of austenite. In order to suppress grain growth, it contributes to miniaturization and high strength, effectively acts on dynamic recrystallization during hot rolling, and has a function of remarkably improving stretch flangeability. For this, it was experimentally found that it is necessary to add acid-soluble Ti so as to be 0.008% or more. For this reason, in this invention, the minimum of acid-soluble Ti was made into 0.008%.
Incidentally, the sufficient heating temperature before hot rolling is required to be sufficient for once dissolving the carbides, nitrides, and carbonitrides produced during casting, and it is necessary to exceed 1200 ° C. is there. On the other hand, it is not preferable to set the temperature higher than 1250 ° C. from the viewpoint of cost and scale generation. Therefore, about 1250 ° C. is preferable.
On the other hand, if the content exceeds 0.2%, not only the effect of deoxidation is saturated, but even if sufficient heating is performed before hot rolling, coarse carbides, nitrides, and carbonitrides are formed. On the contrary, the material is deteriorated, and an effect commensurate with the content cannot be expected. For this reason, in the present invention, the upper limit of the concentration of acid-soluble Ti is set to 0.2%.
Incidentally, the acid-soluble Ti concentration is an analytical method that measures the concentration of Ti dissolved in an acid, and that the dissolved Ti dissolves in an acid and the Ti oxide does not dissolve in an acid. Here, examples of the acid include a mixed acid mixed at a ratio (mass ratio) of hydrochloric acid 1, nitric acid 1, and water 2. By using such an acid, it can be separated into Ti soluble in acid and Ti oxide not soluble in acid, and the acid-soluble Ti concentration can be measured.

(Ca: 0.0005 to 0.0050%)
Ca is an important element in the present invention, and is one of the elements used for complex deoxidation. It controls the form of desulfurization such as spheroidizing sulphides, and MnS, TiMnS, CaS, or (Mn, Ti, Ca) 1 kind or 2 or more S, oxides or oxysulfide complexed precipitated with complexed precipitation is effective to form a composite inclusions, to improve the bending workability stretch flangeability of the steel Can do. In order to obtain these effects, the amount of Ca added is preferably 0.0005% or more. However, when Ca is contained in a large amount, it coarsely precipitates as CaOAl ₂ O ₃ inclusions and CaS (Fe, Mn, Al ₂ O ₃ ) inclusions in the ingot, and their melting point is low at about 1390 ° C. Therefore, it is easily stretched at the time of rolling to become an inclusion which is stretched by about 50 to 100 μm, and on the contrary, bending workability and stretch flangeability (hole expanding workability) are lowered.

By adding Ca after adding (Ce, La, Nd, Pr) described below, it is possible to heterogeneously nucleate as fine (Mn, Ca) S, and 0.0050% at the upper limit of the effect The following Ca concentration is used. Preferably it is 0.001 to 0.0040%. More preferably, it is 0.0012 to 0.0030%.
Furthermore, Ca / T. When O> 0.6 is obtained, the result that the oxygen potential in the molten steel rapidly decreases is obtained, the effect of the combined deoxidation can be enjoyed to the maximum, and the Al ₂ O ₃ activity can be extremely lowered. Therefore, if this component ratio can be achieved, coarse Al ₂ O ₃ -based oxides can be eliminated, surface defects caused by Al ₂ O ₃ -based oxides can be suppressed, and generation of scale defects, red scale, etc. Effective in suppressing generation.

(Total of one or more of Ce, La, Nd, and Pr: 0.001 to 0.01%)
Ce, La, Nd, and Pr reduce Al ₂ O ₃ produced by Al deoxidation and break up Al ₂ O ₃ clusters to be coarsened, tend to become precipitation sites for MnS-based inclusions, and are hard, Ce oxide that is fine and hardly deformed during rolling (for example, Ce ₂ O ₃ , CeO ₂ ), cerium oxysulfide (for example, Ce ₂ O ₂ S), La oxide (for example, La ₂ O ₃ , LaO ₂ ) Lanthanum oxysulfide (eg, La ₂ O ₂ S), Nd oxide (eg, Nd ₂ O ₃ ), Pr oxide (eg, Pr ₆ O ₁₁ ), Ce oxide—La oxide—Nd oxide—Pr oxidation Or inclusions containing cerium oxysulfide-lanthanum oxysulfide as the main phase (50% or more as a guide). Of Ce, La, Nd, and Pr, Ce and La are preferably used.

Here, the inclusions may contain a part of MnO or Al ₂ O ₃ depending on deoxidation conditions. However, if the main phase is the oxide, it sufficiently functions as a precipitation site for MnS inclusions. However, the effect of making the inclusion fine and hard is not impaired.

When the total concentration of one or more of Ce, La, Nd, and Pr (hereinafter sometimes referred to as (Ce + La + Nd + Pr)) is less than 0.001%, SiO ₂ and Al ₂ O ₃ inclusions cannot be reduced. In order to obtain such inclusions, it is experimentally necessary that the total concentration of one or more of Ce, La, Nd, and Pr must be 0.001% or more and 0.01% or less. I found out.

  Specifically, in this composition range, as compared with MnS, oxides or oxysulfides composed of one or more of Ce, La, Nd, and Pr are increasing, and these Ce, La, Nd, and Pr are increased. Inclusions in a form in which MnS is deposited on an oxide or oxysulfide composed of one or two or more of the above increase. That is, MnS is modified with an oxide or oxysulfide composed of one or more of Ce, La, Nd, and Pr. Thus, in order to improve stretch flangeability and bending workability, MnS is deposited on an oxide or oxysulfide composed of one or more of Ce, La, Nd, and Pr, thereby preventing the extension of MnS. Connected.

  On the other hand, when the (Ce + La + Nd + Pr) concentration is more than 0.01%, one or more of cerium oxysulfide, lanthanum oxysulfide, neodymium oxysulfide, and prasedimoxysulfide are produced in large quantities, resulting in coarse inclusions and elongation. Degradation of flangeability and bending workability. Therefore, the upper limit of the (Ce + La + Nd + Pr) concentration is set to 0.01%.

In combined deoxidation in the order of addition of Al, Ti, (Ce, La, Nd, Pr) and Ca, (Ce + La + Nd + Pr) / T. By appropriately performing the deoxidation method so as to obtain O> 0.5, the oxygen potential in the molten steel can be drastically lowered, and the above-described hard spheroidized composite inclusion (REM oxysulfide) Composite inclusions) can be deposited, and deformation of the composite precipitation inclusions can be suppressed even during rolling. Therefore, the stretched flange can be reduced by significantly reducing the stretched coarse MnS inclusions in the steel sheet. The effect that it can improve a property and bending workability is acquired.
Furthermore, Al ₂ O ₃ -based oxide can also be heterogeneously nucleated in a part of the hard composite inclusions, so that the activity of Al ₂ O ₃ can be drastically reduced, and coarse Al _{since 2} O ₃ based oxide is eliminated, it is possible to suppress surface defects due to Al ₂ O ₃ based oxide affects the corrosion of such low oxygen potential of the steel slab or the steel sheet surface, the hydrogen ion concentration of the surface Can be suppressed, and it is drastically effective in generating scale wrinkles and red scales.

The above is the basic component. Next, the selected component will be described.
About the selection component, the presence or absence of addition is arbitrary, and only 1 type may be added and 2 or more types may be added.

In the present invention, any one or two of Nb and V may be added. These elements form carbides, nitrides, and carbonitrides with C or N to promote fine graining of the base material structure and contribute to improvement of toughness. Hereinafter, the reason for limiting the chemical component will be described.
(Nb: 0.001-0.10%)
In order to obtain the above-described composite carbide, composite nitride, etc., the Nb concentration is preferably 0.001% or more. However, even if the Nb concentration exceeds 0.10%, the effect of refining the base material structure is saturated and the manufacturing cost increases. For this reason, the upper limit of the Nb concentration is 0.10%.

(V: 0.01-0.10%)
In order to obtain the above-described composite carbide, composite nitride, etc., the V concentration is preferably 0.01% or more. However, even if the V concentration exceeds 0.10%, the effect is saturated and the production cost is increased. For this reason, the upper limit of the V concentration is 0.10%.

In this invention, you may contain 1 type (s) or 2 or more types of Cu, Ni, Cr, Mo, B further. These elements improve strength and improve the hardenability of the steel. Hereinafter, the reason for limiting the chemical component will be described.
(Cu: 0.1 to 2%)
Cu contributes to the precipitation strengthening and strength improvement of ferrite, and can further be contained as necessary to secure the strength of the steel sheet. To obtain this effect, 0.1% or more may be added. preferable. However, this large amount of Cu deteriorates the balance between strength and ductility. Therefore, the upper limit is 2%.

(Ni: 0.05 to 1%)
Since Ni can strengthen the solid solution of ferrite, it can be contained as necessary to further secure the strength of the steel sheet. To obtain this effect, 0.05% or more may be added. preferable. However, this large amount of Ni deteriorates the balance between strength and ductility. Therefore, the upper limit is 1%.

(Cr: 0.01 to 1%)
In order to further secure the strength of the steel sheet, Cr can be contained as necessary. To obtain this effect, it is preferable to add 0.01% or more. However, this large amount of Cr deteriorates the balance between strength and ductility. Therefore, the upper limit is 1%.

(Mo: 0.01-0.4%)
Mo can be added as necessary to further secure the strength of the steel sheet. To obtain these effects, it is preferable to add 0.01% or more. However, this large amount of Mo deteriorates the balance between strength and ductility. Therefore, 0.4% is made the upper limit.

(B: 0.0003 to 0.005%)
B can be contained as necessary in order to further strengthen the grain boundaries and improve workability. In order to obtain these effects, B is preferably added in an amount of 0.0003% or more. However, even if this B is contained in a large amount exceeding 0.005%, the effect is saturated, and on the contrary, the cleanliness of the steel is impaired and the ductility is deteriorated. Therefore, the upper limit is made 0.005%.

In the present invention, Zr may be further contained. Zr reinforces grain boundaries and improves processability by controlling the morphology of sulfides. Hereinafter, the reason for limiting the chemical component will be described.
(Zr: 0.001 to 0.01%)
Zr is 0.0 in order to obtain the effect of improving the toughness of the base metal by spheroidizing the above-described sulfide.
It is preferable to add 01% or more. However, this large amount of Zr deteriorates the cleanliness of the steel and deteriorates the ductility. Therefore, the upper limit is 0.01%.

  Next, the presence conditions of inclusions in the steel sheet of the present invention will be described. The steel sheet here means a rolled sheet obtained through hot rolling or further cold rolling. Moreover, the presence conditions of the inclusion in the steel plate of this invention are prescribed | regulated from various viewpoints.

In order to obtain a steel sheet excellent in stretch flangeability and bending workability, it is important to reduce as much as possible the stretched and coarse MnS-based inclusions in the steel sheet, which are likely to become the starting point of crack generation and the path of crack propagation.
As described above, the present inventor deoxidized with Al, added Ti, and then added one, two, three, or four of Ce, La, Nd, and Pr, followed by deoxidation, and then Ca In the molten steel that has been combined deoxidized by adding (Ce + La + Nd + Pr) / T. O> 0.5, and Ca / T. When O> 0.6 was obtained, the result was that the oxygen potential in the molten steel suddenly decreased.

Because of the combined deoxidation effect, the Al ₂ O ₃ activity can be extremely low, so that the inclusion form is fine and hard Ce oxide, La which occupies most of the inclusion slightly containing Al ₂ O ₃ , La oxide, Nd oxide, Pr oxide, Se Liu arm oxysulfide, lanthanum oxysulfide, neodymium oxysulfide is praseodymium oxysulfide and Ca oxides also properly Ca oxysulfide complex precipitated, further MnS is put analysis, different It was found to form a composite inclusion with an inclusion phase of components. Further, it was found that the number density of fine inclusions having an equivalent circle diameter of 2 μm or less increased rapidly and the fine inclusions were dispersed in the steel.

Furthermore, since the fine composite inclusions are not easily deformed during rolling, it has been found that the stretched coarse MnS inclusions are remarkably reduced in the steel sheet, and the stretch flangeability and bending workability are excellent. Moreover, if this component ratio can be achieved, coarse Al ₂ O ₃ -based oxides can be eliminated, surface defects caused by Al ₂ O ₃ -based oxides can be suppressed, and generation of scale defects, red scale, etc. It has also been found that it is effective in suppressing the occurrence.

  Since these fine inclusions are difficult to agglomerate, the shape is almost spherical or spindle-shaped. In addition, it is 3 or less, preferably 2 or less when expressed in terms of major axis / minor axis (hereinafter sometimes referred to as “stretch ratio”). The spherical inclusion in the present invention does not mean a perfect sphere, but includes a slightly distorted spindle-like sphere. These inclusions are called spherical inclusions.

Experimentally, identification was easy by observation with a scanning electron microscope (SEM) or the like, and attention was paid to the number density of inclusions having an equivalent circle diameter of 5 μm or less. Incidentally, the lower limit value of the equivalent circle diameter is not particularly specified, but it is preferable to target inclusions of about 0.5 μm or more as the size that can be counted with numbers. Here, the equivalent circle diameter is defined as (major axis × minor axis) ^0.5 obtained from the major axis and minor axis of the inclusion observed in the cross section.
These composite inclusions described above form a large number of composite spherical inclusions having a circle-equivalent diameter of 0.5 to 5 μm, making it difficult to serve as a starting point for crack generation and a path for crack propagation. Therefore, it is thought that it contributes to relaxation of stress concentration and leads to improvement of stretch flangeability and bending workability.

  On the other hand, the present inventor investigated whether stretched and coarse MnS-based inclusions that tend to become crack initiation points and crack propagation paths can be reduced in the steel sheet.

The present inventor has found through experiments that if the equivalent circle diameter is less than 1 μm, even stretched MnS is harmless as a starting point of cracking and does not deteriorate stretch flangeability and bending workability. Inclusions with an equivalent circle diameter of 1 μm or more can be easily observed with a scanning electron microscope (SEM), etc. Therefore, the shape and composition of the inclusions with an equivalent circle diameter of 1 μm or more in a steel sheet are investigated and stretched. The distribution state of the produced MnS inclusions was evaluated.
In addition, although the upper limit of the circle equivalent diameter of MnS is not specified in particular, MnS of about 1 mm may be observed in practice.

  The ratio of the number of stretched inclusions was determined by analyzing the composition of a plurality of inclusions (for example, 50) having a circle-equivalent diameter of 1 μm or more selected at random using SEM, and measuring the major axis and minor axis of the inclusions from the SEM image. To do. Here, the elongated inclusions are defined as inclusions having a major axis / minor axis (ratio of stretching) exceeding 3, and the number of the detected elongated inclusions is the total number of investigated inclusions (50 in the above example). The number ratio of the above-described stretched inclusions can be determined by dividing by the number.

The reason why the stretching ratio was set to 3 or less was that inclusions exceeding the stretching ratio of 3 in the comparative steel sheet to which Ce, La, Nd, and Pr were not added were mostly Ce when MnS, Ce, La, Nd, and Pr were added. , La, Nd, Pr oxide and oxysulfide as the core, MnS precipitates around it, low melting point CaO—Al ₂ O ₃ type inclusions and coarse stretched CaS This is because. In addition, although the upper limit of the extending | stretching ratio of MnS is not prescribed | regulated in particular, MnS of about 50 extending | stretching ratio may be observed actually.

As a result, in all the inclusions having an equivalent circle diameter of 1 μm or more, the stretch flangeability and the bending workability are improved in the steel sheet whose form is controlled so that the number ratio of inclusions having a drawing ratio of 3 or less is 50% or more. There was found.
That is, when the number ratio of inclusions with a stretching ratio of 3 or less is less than 50%, MnS having Ce and La oxides and oxysulfide as the core when MnS, Ce, and La, which are likely to start cracking, are added as the core. The number ratio of inclusions in the case of depositing around, low-melting point CaO-Al ₂ O ₃ inclusions and coarsely extending CaS becomes too large, and stretch flangeability and bending workability deteriorate.
Therefore, in the present invention, the number ratio of inclusions having a stretching ratio of 3 or less is desirably 50% or more.

  Moreover, since the stretch flangeability and bending workability are so good that there are few stretched MnS type inclusions etc., the lower limit of the number ratio of the stretch inclusion exceeding the stretch ratio 3 includes 0%. Here, the inclusion having an equivalent circle diameter of 1 μm or more and the lower limit of the number ratio of the drawn inclusions exceeding the draw ratio of 3 means 0%, but is an inclusion having an equivalent circle diameter of 1 μm or more. This is the case where there is no material with a stretch ratio exceeding 3, or even when the stretch inclusion exceeds the stretch ratio 3, the equivalent circle diameter is less than 1 μm.

  Further, it was confirmed that the maximum equivalent circle diameter of the stretched inclusions was smaller than the average grain size of the structure crystals, which is considered to be a factor that the stretch flangeability and the bending workability could be greatly improved.

In addition, since the composite spherical inclusion having a circle equivalent diameter of 0.5 to 5 μm is a hard inclusion having a high melting point, it does not easily deform during rolling, and is not stretched even in a steel plate. That is, it is a spherical or spindle-shaped inclusion (generically referred to as a spherical shape in the present invention).
Here, the spherical inclusions judged not to be stretched are not particularly defined, but are inclusions having a stretching ratio of 3 or less in the steel sheet, preferably inclusions of 2 or less. In addition, since the spherical inclusion that is determined not to be stretched is completely spherical, the stretch ratio is 1, so the lower limit of the stretch ratio is 1.

This investigation of the number ratio of inclusions was carried out in the same manner as the number ratio investigation of stretched inclusions. As a result, the composite inclusion containing Ce, La, Nd, and Pr components forms one composite spherical inclusion having a circle-equivalent diameter of 0.5 to 5 μm, and the ratio of the number of the inclusions is 0. It has been found that the stretch flangeability and the bending workability are improved in the steel plate whose precipitation is controlled to be 30% or more of the total number of inclusions having a size of 5 to 5 μm.
If the number ratio is less than 30%, the number ratio of the stretched inclusions of MnS increases correspondingly, and the stretch flangeability and bending workability deteriorate, which is not preferable.

  For this reason, the number ratio of one compounded spherical inclusion having a circle equivalent diameter of 0.5 to 5 μm is set to 30% or more. Here, the number ratio is obtained by measuring the major axis and minor axis of 50 stretch inclusions randomly selected using SEM from the SEM image. And the number ratio of the above-mentioned extending | stretching inclusion can be calculated | required by remove | dividing the number of the extending | stretching inclusions whose major axis / short diameter (stretching ratio) is 3 or less by the total number of inclusions investigated (50).

  The stretch flangeability and bending workability are better when a large number of composite spherical inclusions having a circle-equivalent diameter of 0.5 to 5 μm are deposited. Therefore, the upper limit of the number ratio is 100. %including.

In addition, since one compounded spherical inclusion having a circle equivalent diameter of 0.5 to 5 μm is unlikely to be deformed even during rolling, the circle equivalent diameter is not particularly defined within this range, and is 1 μm. That's all. However, if it is too large, there is a concern that cracking will start, so the upper limit is preferably about 5 μm.
On the other hand, this composite inclusion is not easily deformed during rolling, and when the equivalent circle diameter is less than 0.5 μm, it does not become a starting point for cracking. Therefore, the lower limit of the equivalent circle diameter is not particularly specified. .

  Next, the existence condition of the composite inclusions in the steel sheet of the present invention described above is defined by the number density of inclusions per unit volume.

The particle size distribution of the inclusion was carried out by SEM evaluation of the electrolytic surface by the speed method. The SEM evaluation of the electrolytic surface by the speed method is to evaluate the size and number density of inclusions by polishing the surface of the sample piece, performing electrolysis by the speed method, and directly observing the sample surface by SEM.
The speed method is a method in which the sample surface is electrolyzed using 10% acetylacetone-1% tetramethylammonium chloride-methanol to extract inclusions. As the amount of electrolysis, the amount of electrolysis per cm 2 area of the sample surface is used. Was electrolyzed until 1C was reached. The SEM image of the surface electrolyzed in this manner was subjected to image processing, and the frequency (number) distribution with respect to the equivalent circle diameter was obtained. The average equivalent circle diameter was calculated from the frequency distribution of the particle diameters.

  On the other hand, the presence condition of one composite sphere or spindle-shaped inclusion having a circle-equivalent diameter of 0.5 to 5 μm consisting of the composite inclusion in the steel plate of the present invention described above is included in the inclusion. The average composition content of Ce, La, Nd, and Pr was defined.

  The spindle-shaped inclusion is not particularly defined, but is an inclusion having a drawing ratio of 3 or less, preferably 2 or less, in the steel sheet. Here, since the stretching ratio is 1 for a sphere, the lower limit of the stretching ratio is 1.

Composition analysis was performed on such composite inclusions that were not stretched, that is, inclusions with an equivalent circle diameter of 1 μm or more and a stretch ratio of 3 or less.
As a result, when the composite inclusion contains 0.5 to 95% of one or more of Ce, La, Nd, and Pr in an average composition, stretch flangeability and bending workability are improved. There was found.

  When the average content of one or more of Ce, La, Nd, and Pr in the inclusions having an equivalent circle diameter of 1 μm or more and a stretching ratio of 3 or less is less than 0.5% by mass, Since the number ratio of inclusions in the form of is greatly reduced, the number ratio of MnS-based stretch inclusions that are likely to be the starting point of cracking is excessively increased, and stretch flangeability and bending workability are reduced. It is not preferable.

  On the other hand, when the average content of one or more of Ce, La, Nd, and Pr in inclusions with a circle equivalent diameter of 1 μm or more and a stretching ratio of 3 or less exceeds 95%, cerium oxysulfide Since a large amount of lanthanum oxysulfide is produced and coarse inclusions having an equivalent circle diameter of about 50 μm or more are formed, stretch flangeability and bending workability are deteriorated.

Next, the structure of the steel plate will be described.
In the present invention, fine MnS inclusions are precipitated in the ingot, and further, they are not deformed during rolling and are dispersed in the steel plate as fine spherical inclusions that are unlikely to start cracking. It improves workability and is not based on a specific microstructure in the steel sheet.

  Therefore, the microstructure of the steel sheet is not particularly limited. A steel sheet having a structure having bainitic ferrite as a main phase, a composite structure steel sheet having a ferrite phase as a main phase, and a martensite phase and a bainite phase as a second phase. And any structure of a steel sheet having a composite structure composed of ferrite, retained austenite, and low-temperature transformation phase (martensite or bainite).

  Any of these structures is preferable because the crystal grain size can be reduced to 10 μm or less and the hole expandability and bending workability can be improved. When the average particle size exceeds 10 μm, the improvement in ductility, hole expansibility and bending workability tends to be small. In order to improve hole expandability and bending workability, it is more preferably 8 μm or less. However, in general, when it is necessary to obtain excellent stretch flangeability such as undercarriage parts, it is desirable that the ferrite or bainite phase is the largest phase by area ratio although it is slightly inferior in ductility. preferable.

Next, conditions for manufacturing the steel plate described above will be described.
Deoxidation and component adjustment by adding and stirring an alloy such as C and Mn into molten steel that has been decarburized by blowing it in the converter, or decarburized using a vacuum degassing device. To obtain molten steel having a predetermined composition. Specifically, in the refining process in steelmaking, C is 0.03 to 0.25% and Mn is 1.0 to 1.0% in the molten steel treated with P of 0.05% or less and S of 0.0001% or more. These elements are added or adjusted so that 3.0% and N is 0.0005 to 0.01%. Si is not added.

As described above, since it is not necessary to perform desulfurization in the refining step, S can be omitted. However, when molten steel desulfurization is necessary in secondary refining in order to melt extremely low-sulfur steel with S ≦ 20 ppm, component adjustment may be performed by desulfurization. In the treatment in the vacuum degassing apparatus, Al is 0.01% or more of acid-soluble Al. In order to perform Al deoxidation by adding O so as to be 0.0050% or less and to float and separate Al ₂ O ₃ , it is preferable to secure a flying time of about 3 minutes.

  Thereafter, Ti is added so as to be 0.008% or more as acid-soluble Ti, and one or more of Ce, La, Nd, and Pr are added, and Ce, La, Nd, Total of one or more of Pr: 0.001 to 0.01%, (Ce + La + Nd + Pr) / T. The components are adjusted so that O> 0.5.

  By the way, when adding selective elements such as Nb, V, Cu, Ni, etc., do it before adding one, two, three or four of Ce, La, Nd, and Pr, stir well, After the component adjustment of the selected element is performed as necessary, one, two, three, or four kinds of Ce, La, Nd, and Pr are added. Thereafter, the mixture is sufficiently stirred and Ca is added. On a mass basis, Ca / T. The ingredients are adjusted so that O> 0.6, and the molten steel is continuously cast to produce an ingot.

In the present invention, after continuous casting, the steel sheet of the present invention can be obtained through a process according to a conventional method. However, in the conventional method, conditions necessary and preferred conditions for obtaining the steel sheet of the present invention are obtained. Will be described.
For continuous casting, not only is it applied to normal slab continuous casting of about 250 mm thickness, but it is also used for thin slab continuous casting where the mold thickness of blooms and billets and slab continuous casting machines is thinner than usual, for example 150 mm or less. And is fully applicable.

The hot rolling conditions for producing a high-strength hot-rolled steel sheet as the steel sheet of the present invention will be described. It is important that the heating temperature of the slab before hot rolling is higher than 1200 ° C. in order to temporarily dissolve carbonitride in the steel.
When these carbonitrides are dissolved, a ferrite phase preferable for improving ductility can be obtained in the cooling process after rolling. On the other hand, if the heating temperature of the slab before hot rolling exceeds 1250 ° C., the slab surface is significantly oxidized and the yield is lowered. Therefore, the upper limit is preferably set to 1250 ° C.

  After being heated to the above temperature range, normal hot rolling is performed. In the process, the finish rolling completion temperature is important when the structure of the steel sheet is controlled. If the finish rolling completion temperature is less than Ar3 point + 30 ° C., the crystal grain size of the surface layer portion tends to be coarse, which is not preferable in terms of bending workability. On the other hand, if the Ar3 point exceeds + 200 ° C., the austenite grain size after the end of rolling becomes coarse, making it difficult to control the composition and fraction of the phase generated during cooling, so the upper limit is preferably set to the Ar3 point + 200 ° C.

  In addition, when the average cooling rate of the steel sheet after finish rolling is 10 to 100 ° C./second and the coiling temperature is in the range of 450 to 650 ° C., the air cooling is maintained at about 5 ° C./second until 680 ° C. after finish rolling. Then, cooling is performed at a cooling rate of 30 ° C./second or more, and the coiling temperature is set to 400 ° C. or less, and the selection is made according to the target tissue configuration. By controlling the cooling rate and coiling temperature after rolling, the former rolling conditions had one or more microstructures and fractions from polygonal ferrite, bainitic ferrite, and bainite phase. With the latter rolling conditions, a DP steel sheet having a large amount of a polygonal ferrite phase and a martensite phase composite structure excellent in ductility can be obtained.

  If the above average cooling rate is less than 10 ° C./second, pearlite which is unfavorable for stretch flangeability tends to be generated, which is not preferable. On the other hand, there is no need to set an upper limit on the cooling rate in terms of structure control, but too high a cooling rate may cause uneven cooling of the steel sheet, and it is expensive to manufacture equipment that enables such cooling. It is thought that this will lead to an increase in the price of the steel sheet. From such a viewpoint, the upper limit of the cooling rate is preferably set to 100 ° C./second.

  When a high-strength cold-rolled steel sheet is used as the steel sheet of the present invention, the slab after continuous casting produced as described above is heated, and after hot rolling, winding, the steel sheet that has undergone processes such as pickling and skin pass, Cold-rolled and annealed in an annealing process such as batch annealing or continuous annealing to obtain a final cold rolled steel sheet.

  It goes without saying that the high-strength steel plate according to the present invention described above may be applied as a steel plate for electroplating or hot dip galvanizing. Even if electroplating or hot dip galvanization is applied, there is no change in the mechanical properties of the high-strength steel sheet of the present invention.

Examples of the present invention will be described below together with comparative examples. Molten steel having chemical components shown in Table 1 was melted via a converter and an RH process. At that time, when not passing through the molten steel desulfurization process in the secondary refining, S was set to 0.002 to 0.008 mass%. Moreover, when performing molten steel desulfurization, it was set as S <= 20ppm. In order to float and separate Al ₂ O ₃ by adding Al, etc. and adjusting the components as shown in Table 1, after about 3 to 5 minutes, adding Al to deoxidize Al ₂ O ₃ An ascent time of about 3 to 6 minutes was secured.

Thereafter, Ti was added, and the components were adjusted so that Ce, La, Nd, and Pr would be 0.001 to 0.01% depending on the charge of the experiment.
Depending on the charge of the experiment in which the selective element is added, it is performed before adding one, two, three or four of Ce, La, Nd, and Pr. After the adjustment, one, two, three, or four kinds of Ce, La, Nd, and Pr were added. Then, it fully stirred and Ca addition was performed.

  The molten steel thus produced was continuously cast to produce an ingot. For continuous casting, a normal slab continuous casting machine having a thickness of about 250 mm was used. The continuously cast ingot was hot-rolled under the conditions shown in Table 2. That is, the ingot was heated at 1250 ° C. and then subjected to finish rolling through rough rolling. The finish rolling completion temperature was in the range of Ar3 point + 30 ° C. or higher and Ar3 point + 200 ° C. or lower. Here, the calculation derived from the normal component was used to calculate the Ar3 point.

  The average cooling rate of the steel sheet after finish rolling was in the range of 30 to 75 ° C./second. Further, depending on the charge of the experiment, the coiling temperature was set to 450 ° C., and in that case, after finishing rolling, air cooling was maintained at about 5 ° C./second up to 680 ° C., and then cooled at a cooling rate of 30 ° C./second or higher. By this cooling, a steel sheet having one or more structures could be obtained from polygonal ferrite, bainitic ferrite, and bainite phase. On the other hand, depending on the charge of the experiment, a DP steel sheet having a composite structure of a polygonal ferrite phase and a martensite phase could be obtained by winding at 400 ° C.

  When obtaining a high-strength cold-rolled steel sheet, the hot-rolled steel sheet obtained through hot rolling, winding, pickling, skin pass, and other processes was cold-rolled and continuously annealed to obtain a cold-rolled steel sheet. Furthermore, when obtaining the steel plate for plating, it was set as the steel plate for plating by the electroplating or the hot dip galvanizing line.

  The chemical components of the slab are shown in Table 1-1 and Table 1-2. Table 2 shows the hot rolling conditions. As a result, a hot-rolled sheet having a thickness of 3.2 mm was obtained.

  In Tables 1-1 and 2, steel numbers (hereinafter referred to as steel numbers) 1, 3, 5, 7, 9, 11, 13, 15, 17, 19, 21, 23, 25, 27, 29, About 31, 33, 35, 37, 39, it comprises with the composition within the range of the high-strength steel plate concerning the present invention, steel numbers 2, 4, 6, 8, 10, 12, 14, 16, 18, 20, 22, 24, 26, 28, 30, 32, 34, 36, 38, and 40 are configured as slabs that deviate from the range of the high strength steel sheet according to the present invention.

  By the way, in this table 1, steel number 1 and steel number 2, steel plate 3 and steel number 4, steel number 5 and steel number 6, steel number 7 and steel number 8, steel number 9 and steel number 10, steel number 11 Steel No. 12, Steel No. 13 and Steel No. 14, Steel No. 15 and Steel No. 16, Steel No. 17 and Steel No. 18, Steel No. 19 and Steel No. 20, Steel No. 21 and Steel No. 22, Steel No. 23 and Steel No. 24, Steel No. 25 and Steel No. 26, Steel No. 27 and Steel No. 28, Steel No. 29 and Steel No. 30, Steel No. 31 and Steel No. 32, Steel No. 33 and Steel No. 34, Steel No. 35 and Steel No. 36, The steel numbers 37 and 38, and the steel numbers 39 and 40 can be compared with each other so that Ce + La and the like are different from each other after they are composed of substantially the same composition.

  In Table 2, as Condition A, the heating temperature is 1250 ° C., the finish rolling completion temperature is 845 ° C., the cooling rate after finish rolling is 75 ° C./second, and the winding temperature is 450 ° C. As condition B, the heating temperature is 1250 ° C., the finish rolling completion temperature is 860 ° C., and after the finish rolling is maintained at about 5 ° C./second until 680 ° C. After that, the cooling rate of 30 ° C./second or more and the winding temperature are 400 ° C. It is said. As condition C, the heating temperature is 1250 ° C., the finish rolling completion temperature is 825 ° C., the cooling rate after finish rolling is 45 ° C./second, and the winding temperature is 450 ° C. As Condition D, the heating temperature is 1250 ° C., the finish rolling completion temperature is 825 ° C., the cooling rate after finish rolling is 30 ° C./second, and the winding temperature is 400 ° C.

  For Steel No. 1 and Steel No. 2, Condition B, for Steel No. 3 and Steel No. 4, Condition B, for Steel No. 5 and Steel No. 6, Condition A, Furthermore, for Steel No. 7 and Steel No. 8, Condition A, for Steel No. 9 and Steel No. 10, Condition A, and for Steel No. 11 and Steel No. 12, Condition C. By applying condition B to steel numbers 13 and 14, and applying condition D to steel numbers 35 and 36, the influence of the chemical composition under the same production conditions is achieved. It is possible to compare.

  The critical bending radius (mm) was investigated as the strength (MPa), ductility (%), stretch flangeability (λ%), and bending workability of the basic properties of the steel sheet thus obtained. In addition, as for the presence of the stretched inclusions in the steel sheet, the inclusion has an area number density of inclusions of 2 μm or less and a stretching ratio of 3 or less for all inclusions of about 1 μm or more by observation with an optical microscope or SEM. For the product, the number ratio and the average equivalent circle diameter (here, the average is an arithmetic mean, and the same applies hereinafter) were examined.

Furthermore, as an existence state of the unstretched inclusions in the steel sheet, all of Ce, La, Nd, Pr, Al, Ti, and Ca are used for inclusions of about 1 μm or more (0.5 to 5 μm). Or an inclusion phase containing two or more, and containing one or two of O and S, and one or more of Ce, La, Nd, Pr, Ti, and Mn, and There are inclusion phases containing Ca, S and inclusion phases containing one or more of Ti, Mn, and S, and one or more inclusion phases out of the three inclusion phases The number ratio of composite inclusions consisting of, and the number ratio of inclusions with a stretching ratio of 3 or less and one kind of Ce, La, Nd, Pr in inclusions with a stretching ratio of 3 or less The average value of the total content of two or more types was examined.

  The reason why inclusions of about 1 μm or more are targeted is that observations are easy, and inclusions of less than about 1 μm do not affect the deterioration of stretch flangeability and bending workability.

  The results are shown in Table 3 for each combination of steel and rolling conditions. Strength and ductility were determined by a tensile test of a JIS No. 5 test piece taken from the steel plate in parallel with the rolling direction. Stretch flangeability is measured by measuring the hole diameter D (mm) when a through-thickness crack is generated by punching and expanding a punched hole with a diameter of 10 mm in the center of a 150 mm x 150 mm steel plate with a 60 ° conical punch. The hole expansion value λ = (D−10) / 10.

  The critical bending radius (mm) used as an index representing bending workability was obtained by a V-bending test using a die having a die and a punch taken from a bending test piece. A die having a V-shaped recess and an opening angle of 60 ° was used. A punch having a convex portion that fits into the concave portion of the die was used. Prepare a punch with the bend radius of the tip of the punch changed in 0.5mm increments, conduct a bending test, and make the tip of the tip of the punch with the smallest limit that causes cracks in the bent part of the specimen to be tested The curvature radius was obtained and evaluated as the critical bending radius.

  Note that the test piece is a No. 1 test piece defined in the same standard, with a parallel part of 25 mm, a radius of curvature R of 100 mm, and a thickness of 3.0 mm obtained by equally grinding both surfaces of the original plate (hot rolled plate). .

  Further, the inclusions were observed by SEM, and the major axis and the minor axis were measured for 50 inclusions having a circle-equivalent diameter of 1 μm or more selected at random. Further, using the quantitative analysis function of SEM, composition analysis was performed on 50 inclusions with a diameter of 1 μm or more selected at random. Using these results, the number ratio of inclusions with a stretching ratio of 3 or less, the average equivalent circle diameter of inclusions with a stretching ratio of 3 or less, the number ratio of composite inclusions, and the Ce in the inclusion with a stretching ratio of 3 or less, The average value of the total of one or more of La, Nd, and Pr was determined.

  As is clear from Table 3, in the case of odd steel numbers such as steel numbers 1, 3, 5, 7, 9, 11, and 13 to which the method of the present invention is applied, the composite inclusions defined in the present invention are generated. The stretched MnS inclusions could be reduced in the steel sheet. That is, there were fine spherical composite inclusions having a circle-equivalent diameter of 0.5 to 5 μm present in the steel sheet. In addition, the ratio of the number of the composite spherical inclusions having the equivalent circle diameter of 0.5 to 5 μm is 30% or more of the total number of inclusions having the equivalent circle diameter of 0.5 to 5 μm. And the ratio of the number of elongated inclusions having a major axis / minor axis of 3 or less is 50% or more of the total number of inclusions having an equivalent circle diameter of 1 μm or more, and Ce in the inclusions. , La, Nd, and Pr, the total average content of one or more was able to be 0.5% to 95%. In any steel sheet structure, the average crystal grain size was 1 to 8 μm, and the present invention and the comparative example had almost the same average crystal grain size.

  As a result, in comparison with the comparative steel, the steel numbers 1, 3, 5, 7, 9, 11, 13 and so on as the steel of the present invention can be used to obtain a steel plate having excellent stretch flangeability and bending workability. I was able to. However, in the comparative steel (even steel numbers such as steel numbers 2, 4, 6, 8, 10, 12, 14 etc.), the average crystal grain size is over 10 μm and almost contains Ce, La, Nd, and Pr. There is no longer major axis / minor minor axis of 3 or more stretched inclusions, that is, stretched MnS-based inclusions, and the distribution state of the inclusions is different from the distribution state defined in the present invention. It became the starting point of crack generation, and stretch flangeability and bending workability were reduced.

Claims (9)

% By mass
C: 0.03-0.25%,
Si: 0.001 to 0.02%,
Mn: 0.5 to 3.0%
P: 0.05% or less,
T.A. O: 0.0050% or less,
S: 0.0001 to 0.008%,
N: 0.0005 to 0.01%,
Acid-soluble Al: 0.01 to 1.3%
Acid-soluble Ti: 0.008 to 0.20%
Ca: 0.0005 to 0.0050%,
Total of one or more of Ce, La, Nd and Pr: 0.001 to 0.01%,
Further, on a mass basis, (Ce + La + Nd + Pr) / T. O> 0.5, and Ca / T. O> 0.6
The balance is a steel plate of chemical composition consisting of iron and inevitable impurities,
The steel sheet contains one or more of Ce, La, Nd, Pr, Al, Ti, Ca, and an inclusion phase containing one or two of O, S, and
An inclusion phase containing one or more of Ce, La, Nd, Pr, Ti, Mn, and containing Ca, S;
There is an inclusion phase containing one or more of Ti, Mn, S,
Of the three inclusion phases, one or more inclusion phases are combined, and the fine and hard Ce oxide, La oxide, Nd oxide, Pr oxide, and cerium oxy occupy most of the inclusion phase. A composite inclusion in which sulfide, lanthanum oxysulfide, neodymium oxysulfide, praseodymium oxysulfide and Ca oxide or Ca oxysulfide are compositely precipitated, and further MnS inclusions are precipitated, and the equivalent circle diameter is 0.5 to 5 μm. It forms a size one spherical composite inclusions state, and are more than 30% of the total inclusions number of the spherical composite inclusions number proportion the size of the circle equivalent diameter 0.5~5μm of the spherical For inclusions having a circle equivalent diameter of 1 μm or more of the composite inclusion, the ratio of the number of inclusions having a major axis / minor axis of 3 or less is 50% or more of the total number of inclusions having a circle equivalent diameter of 1 μm or more, Luo, the major axis / minor axis is contained in the 3 following inclusions, Ce, La, Nd, 0.5 to 95% by mass Rukoto one or more total the average composition of the Pr High strength steel sheet with excellent stretch flangeability and bending workability. The high-strength steel sheet excellent in stretch flangeability and bending workability according to claim 1, wherein an average grain size of crystals in the structure of the steel sheet is 10 μm or less. Furthermore, in mass%,
Nb: 0.001 to 0.10%,
V: 0.01-0.10%
The high-strength steel sheet excellent in stretch flangeability and bending workability according to claim 1 or 2 , wherein any one or two of these are contained. Furthermore, in mass%,
Cu: 0.1 to 2%,
Ni: 0.05 to 1%,
Cr: 0.01-1%,
Mo: 0.01 to 0.4%,
B: 0.0003 to 0.005%
The high-strength steel sheet excellent in stretch flangeability and bending workability according to any one of claims 1 to 3 , characterized in that any one or more of these are contained. Furthermore, in mass%,
Zr: 0.001 to 0.01%
The high-strength steel sheet excellent in stretch flangeability and bending workability according to any one of claims 1 to 4 , characterized by comprising: In the refining process in steelmaking, in mass%, P is 0.05% or less, S is 0.0001% or more, C is 0.03 to 0.25%, Si is not added, Mn is It is added or adjusted so that 1.0 to 3.0% and N is 0.0005 to 0.01%, and then Al is 0.01% or more with acid-soluble Al. O is added so that it becomes 0.0050% or less, and then Ti is added so that it becomes 0.008% or more as acid-soluble Ti, and then, one or two of Ce, La, Nd, Pr More seeds were added, and on a mass basis, (Ce + La + Nd + Pr) / T. After the total of one or more of O> 0.5, Ce, La, Nd, and Pr is 0.001 to 0.01%, Ca is added, and further, on a mass basis, Ca / T . The high-strength steel sheet excellent in stretch flangeability and bending workability according to claim 1 or 2 , wherein O> 0.6 and Ca: 0.0005 to 0.0050% are added or adjusted. Method of melting molten steel. In the refining step, after deoxidizing with Al and adding Ti, before adding one or more of Ce, La, Nd, and Pr, Nb is further added by 0.001 to 0 by mass%. .10%, V is added so as to be any one or two of 0.01 to 0.10%, and high in stretch flangeability and bending workability according to claim 6 A method for producing molten steel for high-strength steel sheets. In the refining step, after deoxidizing with Al and adding Ti, before adding one or more of Ce, La, Nd and Pr, Cu is further added by 0.1 to 2% by mass. %, Ni 0.05-1%, Cr 0.01-1%, Mo 0.01-0.4%, B 0.0003-0.005%, one or more The method for melting molten steel for high-strength steel sheets excellent in stretch flangeability and bending workability according to claim 6 or 7 , wherein the molten steel is added so that In the refining step, after deoxidizing with Al and adding Ti, before adding one or more of Ce, La, Nd, and Pr, Zr is further added in 0.001 to 0 by mass%. The method for melting molten steel for high-strength steel sheets excellent in stretch flangeability and bending workability according to any one of claims 6 to 8 , characterized by being added so as to be 0.01%.