KR20080038261A - High strength thin steel sheet excellent in hole expansibility and ductility - Google Patents

Abstract

A high strength thin steel sheet excellent in hole expansibility and ductility, characterized in that it has a chemical composition in mass %: C: 0.01 to 0.20 %, Si: 1.5 % or less, Al: 1.5 % or less, Mn: 0.5 to 3.5 %, P: 0.2 % or less, S: 0.0005 % to 0.009 %, N; 0.009 % or less, Mg: 0.0006 to 0.01 %, O: 0.005 % or less, one or both of Ti: 0.01 to 0.20 % and Nb: 0.01 to 0.10 %, and the balance: Fe and inevitable impurities, with the proviso that Mn %, Mg %, S % and O % satisfy the following formula: [Mg %] >= ([O %]/16 X 0. 8) X 24 -------(1) [S %] <= ([Mg %]/24 -[O %]/16 X 0.8 + 0.00012) X 32 --(2) [S %] <= 0.0075/[Mn %] -------(3), and has a steel structure comprising ferrite, bainite and martensite as main components.

Description

High strength steel sheet with excellent hole expandability and ductility {HIGH STRENGTH THIN STEEL SHEET EXCELLENT IN HOLE EXPANSIBILITY AND DUCTILITY}

The present invention is a high-strength steel sheet mainly having a sheet thickness of about 6.0 mm or less, which is mainly used as an automotive steel sheet to be pressed, and has a tensile strength of 590 N / mm 2 or more, or 980 N / mm 2 or more, and excellent hole expandability and ductility. It relates to a manufacturing method.

In recent years, demand for reducing the weight of the vehicle body as a measure for improving fuel efficiency of automobiles and reducing costs by integrally molding parts has been developed, and development of hot rolled high strength steel sheets excellent in press formability has been in progress. BACKGROUND ART Conventionally, as a hot rolled steel sheet for processing, a dual phase steel sheet composed of a ferrite martensite structure is known.

The two-phase structure steel sheet is composed of a composite structure of a soft ferrite phase and a hard martensite phase, and there is a problem in that the hole expandability is inferior because voids are generated and cracks occur at the interfaces of two phases with significantly different hardness. It was unsuitable for the use which requires high hole expandability, such as back.

On the other hand, Japanese Patent Laid-Open Publication No. Hei 4-88125 and Japanese Patent Laid-Open Publication No. Hei 3-180426 have proposed a method for producing a hot rolled steel sheet having excellent hole expandability by a structure mainly composed of bainite. Due to the deterioration of the characteristics, there was a limit to the applied parts.

As a technique for achieving both hole expandability and ductility, Japanese Patent Laid-Open Publication No. Hei 6-293910, Japanese Patent Laid-Open Publication No. 2002-180188, Japanese Patent Laid-Open Publication No. 2002-180189 and Japanese Patent Laid-Open Publication No. 2002-180190 disclose ferrite + bay. Although a steel sheet based on a mixed structure of knight has been proposed, a higher hole expandability is required against the background of a lighter weight of the automobile, a complicated part, and the like, and a high workability and a high strength that are not fully supported by the above technology are required. .

In addition, the present inventors found that in Japanese Unexamined Patent Application Publication Nos. 2001-342543 and 2002-20838, the state of cracking of a punched hole is important as a means for improving hole expandability without involving deterioration of elongation. It has been found that by miniaturization of (Ti, Nb) N, fine homogeneous voids are formed in the end face of the punching hole to reduce the concentration of stress in the hole expanding process and improve the hole expandability.

As the means for miniaturizing this (Ti, Nb) N, use of an oxide of Mg system has been proposed. In the present invention, however, only the oxide is controlled. However, since oxygen has little degree of freedom and limited free oxygen after deoxidation, the total amount is small, and it is difficult to obtain a predetermined dispersion state, and thus it is difficult to obtain a sufficient effect.

SUMMARY OF THE INVENTION The present invention has been made to solve the above problems, and provides a high strength steel sheet having a tensile strength of 590 N / mm 2 or more, or 980 N / mm 2 or more, and having excellent hole expandability and ductility.

Since the present inventors improve the hole expandability by relieving the concentration of stress during hole expansion by generating fine uniform voids in the cross section of the punched hole, various experiments and studies on the method of miniaturization of (Ti, Nb) N are carried out. Repeated.

As a result, although sulfides are known to cause deterioration of pore expandability, Mg sulfides precipitated at high temperature act as nuclei for the formation of (Ti, Nb) N precipitates, and Mg sulfides precipitated at low temperature are (Ti, It has been found that the competitive precipitation with Nb) N has an effect of inhibiting the growth of (Ti, Nb) N, and consequently, the Mg-based sulfide contributes to the improvement of pore expandability due to TiN miniaturization.

In order to avoid the precipitation of Mn-based sulfides and to obtain the above-mentioned action by the precipitation of Mg-based sulfides, it is necessary to add an addition amount of O, Mg, Mn, and S under arbitrary conditions, thereby using Mg-based oxides alone. It has been found that uniform refinement of finer (Ti, Nb) N can be easily achieved as compared with the above. And based on this knowledge, the following invention was achieved.

(1) at mass%,

C: 0.01% or more, 0.20% or less,

Si: 1.5% or less,

Al: 1.5% or less,

Mn: 0.5% or more, 3.5% or less,

P: 0.2% or less,

S: 0.0005% or more, 0.009% or less,

N: 0.009% or less,

Mg: 0.0006% or more, 0.01% or less,

O: 0.005% or less,

And

Ti: 0.01% or more, 0.20% or less,

Nb: 0.01% or more and 0.10% or less

1 or 2 of the compound, the remainder being made of iron and inevitable impurities, and Mn%, Mg%, S% and O% satisfy the formulas 1 to 3, and the steel structure is ferrite, A high-strength steel sheet excellent in hole expandability and ductility, characterized by a structure mainly composed of one or two or more of bainite and martensite.

[Mg%] ≧ ([O%] / 16 × 0.8) × 24... (Equation 1)

[S%] ≤ ([Mg%] / 24-[O%] / 16 x 0.8 + 0.00012) x 32. (Equation 2)

[S%] ≤ 0.0075 / [Mn%]. (Equation 3)

(2) Furthermore, in the composite precipitates of MgO, MgS and (Nb, Ti) N, the precipitates of 0.05 μm or more and 3.0 μm or less contain 5.0 × 10 ² or more and 1.0 × 10 ⁷ or less per square mm. The high strength steel sheet excellent in the hole expandability and ductility as described in said (1) characterized by the above-mentioned.

(3) The high strength steel sheet excellent in the hole expandability and ductility as described in said (1) characterized by further satisfy | filling Formula 4 by Al% and Si% by mass%.

[Si%] + 2.2 × [Al%]> 0.35. (Equation 4)

(4) in mass%,

Moreover, Al% and Si% satisfy | fill Formula 4, The high strength steel plate excellent in the hole expandability and ductility as described in said (2).

[Si%] + 2.2 × [Al%]> 0.35. (Equation 4)

(5) At mass%, Ti%, C%, Mn% and Nb% further satisfy the equations 5 to 7, while the steel structure is the structure mainly composed of bainite, and the strength is greater than 980 N / mm 2. The high strength steel sheet excellent in the hole expandability and ductility in any one of said (1)-(4) characterized by the above-mentioned.

0.9 ≦ 48/12 × [C%] / [Ti%] <1.7... (Eq. 5)

50227 × [C%]-4479 × [Mn%]> -9860. (Equation 6)

811 x [C%] + 135 x [Mn%] + 602 x [Ti%] + 794 x [Nb%]> 465. (Eq. 7)

(6) At mass%, while C%, Si%, Al% and Mn% further satisfy Equation 8, the steel structure is a structure mainly composed of ferrite and martensite, and the strength is greater than 590 N / mm 2. The high strength steel sheet excellent in the hole expandability and ductility in any one of said (1)-(4) characterized by the above-mentioned.

-100 ≤ -300 [C%] + 105 [Si%]-95 [Mn%] + 233 [Al%]. (Eq. 8)

(7) In the crystal grains of the steel structure, there are 80% or more of crystal grains having a ratio of short diameter (ds) to long diameter (dl) (ds / dl) of 0.1 or more, wherein the hole described in (6) above. High strength steel sheet with excellent expandability and ductility.

(8) The high strength steel sheet excellent in the hole expandability and ductility as described in said (7) in which the crystal grain of the ferrite of the said steel structure WHEREIN: 80% or more of crystal grains with a particle diameter of 2 micrometers or more exist.

(9) The mass%, C%, Si%, Mn% and Al% more satisfy the formula 8, while the steel structure is a structure mainly composed of ferrite and bainite, the strength is more than 590 N / mm 2 The high strength steel sheet excellent in the hole expandability and ductility in any one of said (1)-(4) characterized by the above-mentioned.

-100 ≤ -300 [C%] + 105 [Si%]-95 [Mn%] + 233 [Al%]. (Eq. 8)

(10) The hole according to the above (9), wherein in the grain of the steel structure, 80% or more of crystal grains having a ratio of short diameter (ds) to long diameter (dl) (ds / dl) of 0.1 or more are present. High strength steel sheet with excellent expandability and ductility.

(11) The high strength steel sheet excellent in the hole expandability and ductility as described in said (10) in which the crystal grain of the ferrite of the said steel structure WHEREIN: 80% or more of crystal grains with a particle diameter of 2 micrometers or more exist.

(12) The rolling of the steel of the component composition according to any one of the above (1) to (4) is terminated at the rolling end temperature of the Ar ₃ transformation point or more, and then cooled at a cooling rate of 20 ° C / sec or more, and then 300 ° C. A method for producing a high strength steel sheet having excellent hole expandability and ductility, wherein the steel sheet is wound up and has a structure mainly composed of ferrite and martensite, and a high strength steel sheet having a strength of more than 590 N / mm 2.

(13) The rolling of the steel of the component composition according to any one of the above (1) to (4) is terminated at the rolling end temperature of the Ar ₃ transformation point or more, and then 650 ° C to 750 ° C at a cooling rate of 20 ° C / sec or more. Cooled to and then air-cooled at the above temperature for 15 seconds or less, then cooled again, wound at less than 300 ° C, and the steel structure is a structure mainly composed of ferrite and martensite, and the strength is higher than 590 N / mm 2 A method for producing a high strength steel sheet excellent in hole expandability and ductility, characterized by producing a thin steel sheet.

(14) The steel of the component composition described in any one of the above (1) to (4) is terminated at the rolling end temperature of the Ar ₃ transformation point or more, and then cooled at a cooling rate of 20 ° C / sec or more, and then 300 ° C. The high-strength steel sheet excellent in hole expandability and ductility, characterized in that the steel sheet is wound at 600 ° C. or lower, and the steel structure is mainly composed of ferrite and bainite, and the strength is greater than 590 N / mm 2. Method of preparation.

(15) The rolling of the steel of the component composition according to any one of the above (1) to (4) is terminated at the rolling end temperature of the Ar ₃ transformation point or more, and then 650 ° C to 750 at a cooling rate of 20 ° C / sec or more. After cooling to ℃, and then air-cooled at the above temperature for 15 seconds or less, and then again cooled, wound up at 300 ℃ or more, 600 ℃ or less, the steel structure mainly composed of ferrite and bainite, the strength is 590 N / A method for producing a high strength steel sheet excellent in hole expandability and ductility, characterized by producing a high strength steel sheet of greater than mm 2.

According to the present invention, in a high strength steel sheet having a strength level of 590 N / mm 2 or 980 N / mm 2 or more, it is possible to supply a high strength steel sheet having an elongation-ductility balance that has not existed in the prior art. Therefore, this invention is very useful in the industry which uses a high strength steel plate as a base material.

The present invention focuses on the end face properties of punching holes in improving hole expandability, and uniformly and finely deposits Mg-based oxides and sulfides by adjusting the amount of O, Mg, Mn, and S added under predetermined conditions. By suppressing the occurrence of coarse cracks at the time of punching and making the end surface properties uniform, the hole expandability is improved.

EMBODIMENT OF THE INVENTION Below, the structural requirements of this invention are demonstrated in detail.

First, the reason for limitation of the component composition of the high strength thin steel plate (steel plate of this invention) of this invention is demonstrated. In addition,% means mass%.

C is an element that affects the workability of steel, and as the content thereof increases, workability deteriorates. In particular, when the content exceeds 0.20%, carbides (pearlite and cementite) detrimental to pore expandability are produced, so the content is 0.20% or less. However, when especially high hole expandability is calculated | required, it is desirable to set it as 0.1% or less. In addition, 0.01% or more is required from the point which ensures the required intensity | strength.

Si is an element effective in suppressing the formation of harmful carbides and increasing the ferrite fraction to improve elongation, and also an element effective in securing material strength by solid melt strengthening. Therefore, although it is preferable to add Si, since the chemical conversion processability falls as an addition amount increases, point weldability also deteriorates, 1.5% is made into an upper limit.

Al, like Si, is an effective element for inhibiting formation of harmful carbides and increasing ferrite fraction to improve elongation. In particular, it is an element necessary in order to make ductility and chemical conversion treatability compatible.

In addition, Al is an element required for deoxidation conventionally, and usually 0.01 to 0.07% is added. However, as a result of intensive studies, the inventors of the present invention do not deteriorate ductility by adding a large amount of Al even in a low Si system. It has been found that the processability can be improved.

However, when the added amount is increased, only the effect of the ductility improvement is saturated, the chemical conversion treatment property is lowered, and the spot weldability is also deteriorated, so the upper limit is 1.5%. In particular, it is preferable to make 1.0% an upper limit on the conditions with severe chemical conversion treatment.

Mn is an element necessary for securing strength, and at least 0.50% of addition is required. And, in order to secure the hardenability and to obtain a stable strength, addition of more than 2.0% is preferable. However, when a large amount is added, micro segregation and macro segregation tend to occur, and these segregation deteriorates hole expandability. Therefore, 3.5% is made into an upper limit.

P is an element which increases the strength of the steel sheet and is an element which improves the corrosion resistance by simultaneous addition with Cu, but when the content is high, P causes deterioration of weldability, workability and toughness. Therefore, content is made into 0.2% or less. Especially when corrosion resistance does not become a problem, it is preferable to make 0.03% or less in consideration of workability.

S is one of the most important addition elements in the present invention. S binds with Mg and forms sulfides to become nuclei of (Ti, Nb) N, and also inhibits the growth of (Ti, Nb) N, thereby contributing to the miniaturization of (Ti, Nb) N, resulting in a dramatic improvement in pore expandability. Cause.

In order to acquire this effect, 0.0005% or more of addition is required, and 0.001% or more of addition is preferable. However, excessive addition forms Mn sulfide and deteriorates pore expandability, so the upper limit is 0.009%.

Since N contributes to the formation of (Ti, Nb) N, a smaller one is preferable in order to secure workability. If it exceeds 0.009%, coarse TiN is produced and workability deteriorates, so the amount of N is made 0.009% or less.

Mg is one of the most important addition elements in the present invention. Mg combines with oxygen to form an oxide, and also Mg combines with S to form a sulfide. The resulting Mg-based oxides and Mg-based sulfides have a smaller precipitate size and a uniformly dispersed distribution state as compared with conventional steel without Mg.

These precipitates finely dispersed in steel contribute to the fine dispersion of (Ti, Nb) N and are effective in improving hole expandability.

However, if it is less than 0.0006%, the effect is inadequate and 0.0006 or more addition is required. In order to fully acquire the effect, addition of 0.0015% or more is preferable.

On the other hand, addition of more than 0.01% not only saturates the improvement effect, but also deteriorates the cleanliness of the steel and deteriorates the hole expandability and ductility, so the upper limit is made 0.01%.

O is one of the most important addition elements in the present invention. It combines with Mg and forms oxides, which contributes to the improvement of pore expandability. However, since excessive addition deteriorates the cleanliness of steel and causes deterioration of elongation, it makes 0.005% an upper limit.

Ti and Nb are one of the most important addition elements in the present invention. Ti and Nb are elements that are effective for increasing strength by forming carbides, and contribute to uniformity of hardness to improve hole expandability. In addition, Ti and Nb form fine and uniform nitrides with Mg-based oxides and Mg-based sulfides as nuclei, and these nitrides form fine voids during punching to suppress stress concentration, thereby suppressing coarse cracks. As a result, it is judged that the hole expandability is remarkably improved.

In order to exhibit these effects effectively, at least 0.01% or more of Nb and Ti are required.

However, when the added amount is excessive, ductility deteriorates due to precipitation strengthening, so that Ti is 0.20% and Nb is 0.10% as an upper limit. These elements are effective even if added alone or in combination.

In addition, in the steel sheet of the present invention, one or two or more of the following elements may be added.

Ca, Zr, and REM are effective for improving hole expandability by controlling the shape of sulfide inclusions. In order to acquire this effect, it is necessary to add at least 1 type, or 2 or more types 0.0005% or more. On the other hand, the addition of a large amount, on the contrary, deteriorates the cleanliness of the steel and impairs hole expandability and ductility. Therefore, an upper limit is made into 0.01%.

Cu is an element which improves corrosion resistance by complex addition with P. In order to acquire this effect, it is preferable to add 0.04% or more. However, since a large amount of addition increases the quenching property and impairs the ductility, the upper limit is made 0.4%.

Ni is an element which suppresses hot cracking when Cu is added. In order to acquire this effect, it is preferable to add 0.02% or more. However, since the addition of a large amount increases the hardenability and impairs the ductility similarly to Cu, the upper limit is made 0.3%.

Mo is an element effective in suppressing formation of cementite and improving hole expandability. In order to acquire this effect, 0.02% or more of addition is required. However, Mo is also an element which raises hardenability, and since excessive addition reduces ductility, an upper limit is made into 0.5%.

V is an element which forms carbide and contributes to securing strength. In order to acquire this effect, 0.02% or more of addition is required. However, since the addition of a large amount reduces the elongation and the addition cost is also high, the upper limit is made 0.1%.

Cr, like V, is an element that forms carbide and contributes to securing strength. In order to acquire this effect, 0.02% or more of addition is required. However, Cr is also an element which improves hardenability, and since a large amount of addition reduces elongation, an upper limit is made into 1.0%.

B is an element effective for improving the secondary processing crack which becomes a problem in super high ten by strengthening a grain boundary. In order to acquire this effect, 0.0003% or more of addition is required. However, since B is an element which improves hardenability, and addition of a large amount reduces ductility, an upper limit is made into 0.001%.

MEANS TO SOLVE THE PROBLEM As a result of earnestly researching in order to solve the said subject, the present inventors refine | purified (Nb, Ti) N finely using Mg type | system | group oxide and Mg type sulfide by adjusting the addition amount of O, Mg, Mn, and S under predetermined conditions. Found it possible.

In other words, by controlling the precipitation temperature of the Mg-based sulfide while sufficiently precipitating the Mg-based oxide and suppressing the precipitation of the Mn-based sulfide, and by depositing the Mg-based sulfide, it becomes possible to use the above-described action as a nucleus and growth inhibition. . For this reason, the following three relational expressions were derived. It demonstrates below.

In the present invention, since Mg sulfide is used in addition to Mg oxide, Mg needs to be added in an amount of at least O. However, although O forms an oxide also with other elements, such as Al, the present inventors earnestly examined and, as a result, the effective O couple | bonded with Mg is 80% of analytical amount, and Mg addition more than this amount acts on the improvement of pore expandability. Necessary to form sufficient sulfides. Therefore, Mg addition amount needs to satisfy Formula (1).

On the other hand, in the formation of Mg sulfide, S is an essential element, but when the amount of S increases, S becomes Mn sulfide. A small amount of precipitated Mn sulfides is present in a complex state with Mg sulfides and does not affect the deterioration of pore expandability, but when precipitated in large amounts, the details are not clear, but affect the characteristics of single precipitates or Mg sulfides. Deteriorates hole expandability. For this reason, S amount needs to satisfy Formula 2 with respect to Mg and an effective O amount.

In addition, under conditions where both the Mn amount and the S amount are large, Mn-based sulfides are precipitated at a high temperature, and the formation of Mg-based sulfides is suppressed, so that sufficient pore expandability cannot be obtained. Therefore, Mn amount and S amount need to satisfy Formula 3.

[Mg%] ≧ ([O%] / 16 × 0.8) × 24... (Equation 1)

[S%] ≤ ([Mg%] / 24-[O%] / 16 x 0.8 + 0.00012) x 32. (Equation 2)

[S%] ≤ 0.0075 / [Mn%]. (Equation 3)

In order to relieve stress concentration at the time of hole expansion processing and to improve hole expandability by generating fine and uniform voids in the cross section of the punching hole, the refinement of (Nb, Ti) N is important. When the size of (Nb, Ti) N is small, it is not a starting point for producing fine and uniform voids, and when it is too large, it is a starting point of coarse cracks.

In addition, when the number of precipitates of this precipitate is small, the number of fine voids generated at the time of punching is insufficient, and it is judged that the effect of suppressing the occurrence of coarse cracks cannot be obtained.

As a result of earnestly examining, the present inventors have found that complex precipitation with MgO and MgS can be used as a method for uniformly and finely depositing (Nb, Ti) N. Although the reason is not determined, it is the complex precipitate of MgO, MgS, and (Nb, Ti) N which are the sizes and precipitate density of the composite precipitate which shows the effect in the composite use of sulfide besides oxide, and are 0.05 micrometer or more and 3.0 micrometer or less It was found that the precipitates of at least need to contain 5.0 × 10 ² or more and 1.0 × 10 ⁷ or less per square mm. At this time, even if Al ₂ O ₃ and SiO ₂ are contained in the composite oxide, the present effect is not impaired, and even if MnS is contained in a small amount, the effect is not impaired.

In addition, the dispersion state of the composite precipitate prescribed | regulated by this invention is quantitatively measured by the following method, for example. An extraction replica sample is prepared from any place of the base steel sheet, and this is observed using a transmission electron microscope (TEM) at a magnification of 5000 to 20,000 times and observed over an area of at least 5000 µm ² or greater, preferably 50000 µm ² or greater. The number of composite inclusions to be measured is converted into the number per unit area.

At this time, identification of oxide and (Nb, Ti) N is performed by composition analysis by energy dispersive X-ray spectroscopy (EDS) attached to TEM, and crystal structure analysis of the electron beam diffraction image by TEM. When it is troublesome to perform all the complex inclusions which measure such identification, the following procedure is simply followed.

First, the number of sizes to be measured is measured by the above-described method by shape and size, and among these, all of the different shapes and sizes are identified by the above-described method for each of 10 or more, and oxides and (Nb, Ti) Calculate the ratio of N. And this ratio is multiplied by the number of inclusions measured initially.

When carbide in steel interferes with the TEM observation, the carbide can be coarsened or dissolved by heat treatment to easily observe the target composite inclusions.

Si and Al are very important elements for controlling the structure to secure ductility. However, in the case of Si, unevenness of the surface called Si scale may occur in the hot rolling process, and thus the appearance of the product is not damaged, and in the case of chemical conversion treatment or coating carried out after pressing, the formation of the chemical conversion treatment film or the coating is poor. Bad adhesion occurs.

For this reason, a large amount of Si may not be added in the use of some chemical conversion treatments. At this time, in order to achieve both ductility and chemical conversion treatment, it is possible to replace Si by Al. However, when the addition amount of Si and Al is large, the ferrite phase fraction is increased so that the target strength cannot be obtained.

Therefore, in order to secure sufficient strength and to ensure ductility, the amount of Si and the amount of Al need to satisfy the expression (4). However, when elongation becomes a subject especially, it is preferable to set it as 0.9 or more.

[Si%] + 2.2 × [Al%]> 0.35. (Equation 4)

Next, the structure of the steel sheet of the present invention will be described.

Since this invention improves the cross-sectional property at the time of punching, even if a steel structure contains any phase among ferrite, bainite, and martensite, a required effect is exhibited.

However, since the steel structure affects the mechanical properties, the structure is controlled in accordance with the mechanical properties of the requirements.

(1) Steel sheet mainly containing bainite (steel sheet B of the present invention)

In order to secure the strength exceeding 980 MPa, it is necessary to use the structure reinforcement as a reinforcing mechanism, and in order to increase the hole expandability, in particular, the structure should be mainly composed of bainite.

At this time, since the ductility is improved when the second phase is made of ferrite, it is preferable to include ferrite as the second phase. In addition, in the steel sheet B of the present invention, even if austenite remains in the structure, the effect of the present invention is not impeded, but coarse cementite and pearlite are not preferable because they reduce the effect of improving the end face properties due to Mg-based precipitates.

Steels with strengths greater than 980 N / mm 2 are ductile and hole expandability deteriorates with increasing strength. MEANS TO SOLVE THE PROBLEM As a result of earnestly researching in order to solve the said subject, the steel structure of a bainite main body as a means to improve the hole expandability by the improvement of the punching end surface property by Mg type | system | group precipitate, and to secure ductility while ensuring strength It has been found that it is effective to define the range of the component amounts of C, Mn, Ti, and Nb in.

That is, three relational expressions shown below were derived by clarifying the maximum use of TiC precipitation reinforcement and the effect on the material of tissue reinforcement by Mn and C. It demonstrates below.

When the amount of C added is smaller than Ti, the elongation is deteriorated due to the increase of the solid molten Ti, so that 0.9? 48/12 x C / Ti. On the other hand, when C is too high compared with Ti, TiC precipitates during hot-rolling heating, and the effect of a strength increase cannot be obtained, and in addition, deterioration of the hole expandability by increase of the amount of C in a 2nd phase is accompanied.

Since this leads to the reduction of the end surface property improvement effect by Mg type | system | group precipitate, 48/12 * C / Ti makes 1.7 an upper limit.

That is, the amount of Ti and the amount of C need to satisfy Expression 5.

0.9 ≦ 48/12 × C / Ti <1.7... (Eq. 5)

In particular, when emphasis is placed on hole expandability, it is preferable to set 1.0 ≦ 48/12 × C / Ti <1.3.

Since ferrite production is suppressed with an increase in the amount of Mn added, the second phase fraction is increased, thereby making it easy to secure the strength but causing a decrease in the elongation. On the other hand, C hardens the second phase to degrade the hole expandability but improves the elongation.

Therefore, in order to secure the elongation required for tensile strength of more than 980 N / mm 2, the amount of C and the amount of Mn need to satisfy the formula (6).

50227 × C-4479 × Mn> -9860. (Equation 6)

In order to secure workability, it is necessary to satisfy the above two equations. In the case of a steel sheet of 780 N / mm 2 level, it is relatively easy to satisfy the above formula 2 while securing the strength, but in order to secure the strength of more than 980 N / mm 2, C which degrades the hole expandability or Mn which degrades the elongation is obtained. The addition of is inevitable.

In order to secure the intensity | strength exceeding 980 N / mm <2>, it is necessary to adjust a component to the range which satisfy | fills Formula 7 while satisfy | filling said two formulas.

811 x C + 135 x Mn + 602 x Ti + 794 x Nb &gt; (Eq. 7)

Next, a manufacturing method is demonstrated.

The finish rolling finish temperature needs to be at least the Ar ₃ transformation point in order to hinder the formation of ferrite and to improve hole expandability. However, when the temperature is too high, the strength is reduced due to the coarsening of the structure and the ductility is lowered.

The cooling rate suppresses carbide formation detrimental to hole expandability, and 20 ° C./sec or more is required to obtain a high hole expansion ratio.

The coiling temperature is set to 300 ° C or higher because martensite is formed at less than 300 ° C and the hole expandability deteriorates.

In addition, the low-temperature generated bainite is not as much as martensite, but when present as the second phase, the hole expandability deteriorates. For this reason, it is preferable to wind up at 350 degreeC or more.

When the coiling temperature exceeds 600 ° C, pearlite and cementite harmful to the hole expandability are produced, so the coiling temperature is set to 600 ° C or lower.

Air cooling during continuous cooling is effective to increase the occupancy of the ferrite phase and to improve the ductility. However, depending on the air-cooling temperature and the air-cooling time, pearlite is generated and conversely, the ductility is lowered, and the hole expandability is remarkably decreased.

When air cooling temperature is less than 650 degreeC, since the pearlite which is harmful to hole expansion property generate | occur | produces early, air cooling temperature shall be 650 degreeC or more.

On the other hand, if the air-cooling temperature is higher than 750 ° C, the production of ferrite is delayed and it is difficult to obtain the effect of the air-cooling, and since the ferrite is easily generated during subsequent cooling, the air-cooling temperature is set to 750 ° C or lower.

Air cooling above 15 seconds not only saturates the increase in ferrite, but also puts a load on the subsequent cooling rate, control of the winding temperature. Therefore, air cooling time shall be 15 second or less.

(2) Steel plate mainly composed of ferrite and martensite (steel plate FM of the present invention)

Since the end face control technique is related to the improvement of the hole expandability of the steel sheet, it is necessary to secure the elongation in the steel structure in order to secure both the ductility and the hole expandability at high values. To do this, it is necessary to make the steel structure mainly composed of ferrite and martensite.

At this time, if the ferrite is present at 50% or more, the ductility can be particularly high, so the ferrite fraction is preferably at least 50%. In addition, in the steel sheet FM of the present invention, even if austenite remains in the structure, the effect of the present invention is not hindered, but coarse cementite and pearlite are not preferable because they reduce the effect of improving the end face properties due to Mg-based precipitates.

In hot rolling, the desired structure must be formed within a short time after the finish rolling, but the influence of the component composition is very strong on the formation of the desired structure. When steel is mainly composed of ferrite and martensite, it is important to secure ferrite fraction to improve ductility.

In order to secure the ferrite fraction effective for improving the ductility, each amount of C, Si, Mn, and Al needs to satisfy the following formula (8). When the value of Equation 8 is less than -100, a sufficient amount of ferrite cannot be obtained and the ductility deteriorates because the second phase fraction increases.

-100 ≤ -300 [C%] + 105 [Si%]-95 [Mn%] + 233 [Al%]. (Eq. 8)

The present inventors intensively studied the means for improving the ductility without reducing the effect of improving the hole expandability due to the improvement of the punching end face properties by the Mg-based precipitate in the steel mainly composed of ferrite and martensite. As a result, it was found that controlling the shape of the ferrite and the ferrite particle size effectively acts as a ductility improving means. It demonstrates below.

The shape of the ferrite particles is one of the important indicators for improving the ductility in the steel sheet FM of the present invention. Generally, in a high alloy component system, there are many ferrite grains extended in the rolling direction. As a result of diligent study by the present inventors, it has been found that these stretched particles cause ductile deterioration, and also the existence probability of grains having a ratio of short diameter (ds) to long diameter (dl) (ds / dl) of less than 0.1 as an index. It was found that lowering is effective.

In order to fully acquire the effect of ductility improvement by controlling ferrite grains, it is necessary for the ferrite crystal to exist 80% or more of crystal grains whose ratio (ds / dl) is 0.1 or more.

Ferrite particle size is one of the important indicators for improving the ductility in the present invention. In general, grains are refined with increasing strength. As a result of intensive studies by the present inventors, it was found that ferrite grown sufficiently in the same strength contributes to the improvement of ductility.

And in order for crystal grain size to fully acquire ductility improvement, it is necessary that 80% or more of crystal grains of the particle diameter of 2 micrometers or more exist in a ferrite crystal grain.

Next, a manufacturing method is demonstrated.

The finish rolling finish temperature needs to be at least the Ar ₃ transformation point in order to hinder the formation of ferrite and to improve hole expandability. However, when the temperature is too high, the strength is reduced due to the coarsening of the structure and the ductility is lowered. Therefore, the temperature is preferably 950 ° C or lower. The cooling rate is required to be at least 20 ° C / s in order to suppress formation of carbides detrimental to hole expandability and to obtain a high hole expansion ratio.

If the coiling temperature is 300 ° C or higher, martensite cannot be produced, and the strength is lowered, so that the predetermined strength cannot be ensured. In order to secure sufficient strength and fully obtain the improvement of elongation by this, it is preferable to make winding temperature 200 degrees C or less.

Air cooling during continuous cooling is effective to increase the occupancy of the ferrite phase and to improve the ductility. However, pearlite is produced depending on the air-cooling temperature and the air-cooling time, and conversely, the ductility is lowered, and the hole expandability is remarkably lowered.

When air cooling temperature is less than 650 degreeC, since the pearlite which is harmful to hole expansion property generate | occur | produces early, air cooling temperature shall be 650 degreeC or more.

On the other hand, if the air cooling temperature is higher than 750 ° C., the formation of ferrite is delayed and it is difficult to obtain the effect of air cooling, and pearlite is easily generated during subsequent cooling, so the air cooling temperature is set to 750 ° C. or lower.

Air cooling in excess of 15 seconds not only saturates the ferrite increase but also puts a load on the subsequent cooling rate and control of the winding temperature. Therefore, air cooling time shall be 15 second or less.

(3) Steel sheet mainly composed of ferrite and bainite (steel sheet FB of the present invention)

Since the end face control technique is a technique related to improvement of hole expandability, hole expandability is also strongly influenced by the ductility of the base material and hole expandability (base characteristics). In particular, peripheral parts and the like have a strong demand for hole expandability, and it is necessary to aim at a steel sheet having a good balance of ductility and hole expandability as a base characteristic, and further improve hole expandability by an end face control technique.

Therefore, the steel structure needs to be composed mainly of ferrite and bainite. At this time, when the ferrite is present at 50% or more, the ductility can be particularly high, so the ferrite fraction is preferably at least 50%.

In addition, in the steel sheet FB of the present invention, even if an austenite phase remains in the structure, the effect of the present invention is not hindered, but coarse cementite and pearlite are not preferable because they reduce the effect of improving the end surface properties due to Mg-based precipitates.

In hot rolling, the desired structure must be formed within a short time after the finish rolling, but the influence of the component composition is very strong on the formation of the desired structure. When the steel structure mainly contains ferrite + bainite, it is important to secure the ferrite fraction in order to improve the ductility.

In order to secure the ferrite fraction effective for improving the ductility, each amount of C, Si, Mn, and Al needs to satisfy the following formula (8). If the value of Equation 8 is less than -100, a sufficient amount of ferrite cannot be obtained, and the ductility deteriorates because the second phase fraction increases.

-100 ≤ -300 [C%] + 105 [Si%]-95 [Mn%] + 233 [Al%]. (Eq. 8)

The present inventors intensively studied the means for improving the ductility without reducing the effect of improving the hole expandability due to the improvement of the punched end face properties by the Mg-based precipitate in the steel mainly composed of ferrite + bainite. As a result, it was found that controlling the shape of the ferrite and the ferrite particle size effectively acts as a ductility improvement means. It demonstrates below.

Ferrite shape is one of the important indicators for improving the ductility in the present invention. Generally, in a high alloy component system, there are many ferrite grains extended in the rolling direction. As a result of diligent study by the present inventors, it has been found that these stretched particles cause ductile deterioration, and also the existence probability of grains having a ratio of short diameter (ds) to long diameter (dl) (ds / dl) of less than 0.1 as an index. It was found that lowering is effective.

In order to fully acquire the effect of ductility improvement by controlling ferrite grains, it is necessary that 80% or more of crystal grains whose ratio (ds / dl) is 0.1 or more exist in a ferrite grain.

Ferrite particle size is one of the important indicators for improving the ductility in the present invention. In general, the grain size is refined with high strength. As a result of intensive studies by the present inventors, it was found that ferrite grown sufficiently in the same strength contributes to the improvement of ductility.

And in order for a grain size to fully contribute to ductility improvement, it is necessary that 80% or more of grains of a particle size of 2 micrometers or more exist in a crystal grain of ferrite.

Next, a manufacturing method is demonstrated.

* Finish rolling temperature needs to be at or above the Ar ₃ transformation point in order to hinder the formation of ferrite and to improve hole expandability. However, when the temperature is too high, the strength is reduced due to the coarsening of the structure and the ductility is lowered. Therefore, the temperature is preferably 950 ° C or lower.

The cooling rate requires 20 ° C./s or more in order to suppress formation of carbides detrimental to hole expandability and to obtain a high hole expansion ratio.

The coiling temperature is set to 300 ° C or higher because martensite is formed at less than 300 ° C and the hole expandability deteriorates.

In addition, the low-temperature generated bainite is not as much as martensite, but when present as the second phase, the hole expandability deteriorates. For this reason, it is preferable to wind up at 350 degreeC or more.

When the coiling temperature exceeds 600 ° C, pearlite and cementite harmful to the hole expandability are produced, so the coiling temperature is set to 600 ° C or lower.

Air cooling during continuous cooling is effective because it increases the occupancy of the ferrite phase to improve ductility. However, pearlite is produced depending on the air-cooling temperature and the air-cooling time, and conversely, the ductility is lowered, and the hole expandability is remarkably lowered.

When air cooling temperature is less than 650 degreeC, since the pearlite which is harmful to hole expansion property generate | occur | produces at an early time, air cooling temperature shall be 650 degreeC or more.

On the other hand, when the air cooling temperature is higher than 750 ° C, the production of ferrite is delayed and it is difficult to obtain the effect of air cooling, and pearlite is easily generated during the subsequent cooling, so the air cooling temperature is set to 750 ° C or lower.

Air cooling, which results in 15 seconds, not only saturates the increase in ferrite, but also puts a load on the subsequent cooling rate, winding temperature control. Therefore, air cooling time shall be 15 second or less.

Next, the present invention will be described based on Examples.

[First Embodiment]

This is an example of the steel F of the present invention.

The steel of the component composition and characteristic values shown in Table 1 and Table 2 was melted and it was set as the slab by continuous casting according to a conventional method. Codes A to Z are steels of the component composition according to the present invention, the steel of a is the amount of C added, the steel of b is the amount of Mn added, the steel of c is added O, the steel of e is added S, the steel of f is added Mg This is outside the scope of the present invention.

In addition, the steel of a is the expression 5, the river b is the expression 3 and the expression 6, the c is the expression 1 and the expression 2, the d is the expression 4, the e is the expression 2 and the expression is 3, The steel of Formula 1, g has Formula 7 outside the scope of the present invention. The number of precipitates in the steel of f is outside the scope of the present invention.

These steels were heated to a temperature of 1200 ° C. or higher in a heating furnace, and were hot rolled steel sheets having a plate thickness of 2.6 to 3.2 mm. Hot rolling conditions are shown in Tables 3 and 4.

In Tables 3 and 4, A4 and J2 are cooling rates, B3 and F3 are air cooling start temperatures, and E3, G3 and Q4 are winding temperatures outside the scope of the present invention, respectively.

The hot rolled steel sheet thus obtained was subjected to a tensile test and a hole expansion test by a JIS No. 5 member. The hole expandability (λ) unreasonably expands a punching hole with a diameter of 10 mm with a 60 ° conical punch, and the hole diameter (d) and the initial hole diameter (dO: 10 mm) at the time when the crack penetrates the plate thickness. It evaluated from (lambda) = (d-dO) / dOx100 from the.

Table 2 shows TS, El, and λ of each test member. Fig. 1 shows the relationship between the strength and the elongation, and Fig. 2 shows the relationship between the strength and the hole expansion (ratio). It can be seen that the steel of the present invention is superior in elongation, hole expansion (ratio), or both characteristics, as compared with the comparative steel. On the other hand, the steel of g1 could not obtain desired strength.

As described above, according to the present invention, a high-strength hot rolled steel sheet excellent in both hole expansion ratio and ductility can be obtained while securing a predetermined strength of 980 N / mm 2.

TABLE 1

TABLE 2

TABLE 3

TABLE 4

(Following Table 3)

Second Embodiment

An embodiment of the present invention steel FM.

The steel of the component composition and characteristic values shown in Table 5 and Table 6 was melted and it was set as the slab by continuous casting according to a conventional method. Codes A to Z are steels of the component composition according to the present invention, the steel of a is the amount of C added, the steel of b is the amount of Mn added, the steel of c is added O, the steel of e is added S, the steel of f is added Mg This is outside the scope of the present invention.

In addition, the steel of b is the formula 3 and 8, the c is the formula 1 and 2, the d is the formula 4, the e is the formula 2 and the equation 3, the steel is f 1 is the scope of the present invention It is. In addition, the number of precipitates in the steel of f and g is outside the scope of the present invention.

These steels were heated to a temperature of 1200 ° C. or higher in a heating furnace, and were hot rolled steel sheets having a plate thickness of 2.6 to 3.2 mm. Hot rolling conditions are shown in Tables 7 and 8.

In Tables 7 and 8, A4 and J2 have cooling rates, B3 and F3 have air cooling start temperatures, and E3, G3 and Q4 have winding temperatures outside the scope of the present invention, respectively.

Thus, the tensile test and hole expansion test by JIS5 member were performed about the hot rolled sheet steel obtained. The hole expandability (λ) unduly expands a punching hole with a diameter of 10 mm with a 60 ° conical punch, from the hole diameter (d) and the initial hole diameter (dO: 10 mm) at the time when the crack penetrates the plate thickness. (lambda) = (d-dO) / dOx100 was evaluated.

TS, El, and λ of each test member are shown in Tables 7 and 8. Fig. 3 shows the relationship between the strength and the elongation, and Fig. 4 shows the relationship between the strength and the hole expansion ratio (ratio). It can be seen that the steel of the present invention is superior in elongation, hole expansion ratio (ratio), or both characteristics as compared with the comparative steel.

In addition, Table 9 and FIG. 5 show the relationship between the ratio of the short diameter ds and the long diameter dl (ds / dl) exceeding 0.1 and the elongation. When this ratio is 80% or more, it turns out that it is stable and a high elongation is obtained.

In addition, Table 10 and FIG. 6 show the relationship between the ratio and the elongation of ferrite grains of 2 µm or more in the ferrite grains. When this ratio is 80% or more, it turns out that it is stable and a high elongation is obtained.

As described above, according to the present invention, a high strength hot rolled steel sheet excellent in both the hole expansion ratio and the ductility can be obtained.

TABLE 5

TABLE 6

TABLE 7

TABLE 8

(Following Table 7)

TABLE 9

TABLE 10

Third Embodiment

It is an Example regarding this invention steel plate FB.

The steel of the component composition and characteristic values shown in Table 11 and Table 12 was melted and it was set as the slab by continuous casting according to a conventional method. Codes A to Z are steels of the component composition according to the present invention, the steel of a is the amount of C added, the steel of b is the amount of Mn added, the steel of c is added O, the steel of e is added S, the steel of f is added Mg This is outside the scope of the present invention.

In addition, the steel of b is represented by Equation 3 and 8, the c is represented by Equation 1 and 2, the d is represented by Equation 4 and 8, the e is represented by Equation 2, It is outside the scope of the invention. In addition, the number of precipitates in the steel of f and g is outside the scope of the present invention.

These steels were heated to a temperature of 1200 ° C. or higher in a heating furnace, and were hot rolled steel sheets having a plate thickness of 2.6 to 3.2 mm. Hot rolling conditions are shown in Table 13 and Table 14.

In Table 13 and Table 14, A4 and J2 are cooling rates, B3 and F3 are air cooling start temperatures, and E3, G3 and Q4 are winding temperatures outside the scope of the present invention, respectively.

Thus, the tensile test and hole expansion test by JIS5 member were performed about the hot rolled sheet steel obtained. The hole expandability (λ) unduly expands a punching hole with a diameter of 10 mm with a 60 ° conical punch, from the hole diameter (d) and the initial hole diameter (dO, 10 mm) at the time when the crack penetrates the plate thickness. (lambda) = (d-dO) / dOx100 was evaluated.

TS, E1, and lambda of each test member are shown in Table 13 and Table 14. Fig. 7 shows the relationship between the strength and the elongation, and Fig. 8 shows the relationship between the strength and the hole expansion ratio. It can be seen that the steel of the present invention is superior in elongation, hole expansion ratio (ratio), or both characteristics as compared with the comparative steel.

In addition, Table 15 and FIG. 9 show the relationship between the ratio of the short diameter ds and the long diameter dl (ds / dl) exceeding 0.1 and the elongation. When this ratio is 80% or more, it turns out that it is stable and a high elongation is obtained. In addition, Table 16 and FIG. 10 show the relationship between the ratio which has a particle diameter of 2 micrometers or more, and an elongation among ferrite crystal grains. When this ratio is 80% or more, it turns out that it is stable and a high elongation is obtained.

As described above, according to the present invention, a high strength steel sheet excellent in both the hole expansion ratio and the ductility can be obtained.

TABLE 11

TABLE 12

TABLE 13

TABLE 14

(Following Table 13)

TABLE 15

TABLE 16

1 is a diagram showing the relationship between tensile strength and elongation.

2 is a diagram showing a relationship between tensile strength and hole expansion ratio.

3 is a diagram showing a relationship between tensile strength and elongation.

4 is a diagram showing a relationship between tensile strength and hole expansion ratio.

5 is a diagram showing a relationship between an elongation and ds / dl.

Fig. 6 is a diagram showing a relationship between an elongation and a ratio of ferrite particles of 2 µm or more.

7 is a diagram showing a relationship between tensile strength and elongation.

8 is a diagram showing a relationship between tensile strength and hole expansion ratio.

9 is a diagram showing a relationship between an elongation and ds / dl.

Fig. 10 is a graph showing the relationship between the elongation and the ratio of ferrite particles of 2 m or more.

Claims (13)

In mass%, C: 0.01% or more, 0.20% or less, Si: 1.5% or less, Al: 1.5% or less, Mn: 0.5% or more, 3.5% or less, P: 0.2% or less, S: 0.0005% or more, 0.009% or less, N: 0.009% or less, Mg: 0.0006% or more, 0.01% or less, O: 0.005% or less, and Ti: 0.01% or more, 0.20% or less, Nb: 0.01% or more, 0.10% or less, Containing one or two of the residues, the remainder being made of iron and unavoidable impurities, and Mn%, Mg%, S% and O% satisfy the formulas 1 to 3, and the steel structure is ferrite, bay In the composite precipitate of MgO, MgS, and (Nb, Ti) N, which is composed of one or two or more kinds of nitrite and martensite, and contains residual austenite, 0.05 µm or more and 3.0 µm or less High-strength steel sheet excellent in hole expandability and ductility, characterized in that precipitates contain at least 5.0 × 10 ² and 1.0 × 10 ⁷ per square mm. [Mg%] ≧ ([O%] / 16 × 0.8) × 24... (Equation 1) [S%] ≤ ([Mg%] / 24-[O%] / 16 x 0.8 + 0.00012) x 32. (Equation 2) [S%] ≤ 0.0075 / [Mn%]. (Equation 3) The high-strength steel sheet having excellent hole expandability and ductility according to claim 1, wherein the relation between Al and Si satisfies Equation 4. [Si%] + 2.2 × [Al%]> 0.35. (Equation 4) The mass% and Ti%, C%, Mn% and Nb% satisfy the formulas 5 to 7, while the steel structure is the structure of bainite and ferrite, and the strength is according to claim 1 or 2. The high strength steel sheet excellent in hole expandability and ductility, characterized by more than 980 N / mm 2. 0.9 ≦ 48/12 × C / Ti <1.7 (Eq. 5) 50227 × C-4479 × Mn> -9860. (Equation 6) 811 x C + 135 x Mn + 602 x Ti + 794 x Nb &gt; (Eq. 7) The mass%, C%, Si%, Al% and Mn% satisfy the formula 8, and the steel structure is the structure of ferrite and martensite, and the strength is 590 N. High strength steel sheet excellent in hole expandability and ductility, characterized in that more than / mm2. -100 ≤ -300 [C%] + 105 [Si%]-95 [Mn%] + 233 [Al%]. (Eq. 8) 5. The hole expandability and ductility according to claim 4, wherein in the grain of the steel structure, there are 80% or more of grains having a ratio of short diameter ds and long diameter dl (ds / dl) of 0.1 or more. This excellent high strength steel sheet. The high-strength steel sheet excellent in hole expandability and ductility according to claim 5, wherein in the crystal grains of ferrite of the steel structure, 80% or more of crystal grains having a particle diameter of 2 µm or more are present. The mass%, C%, Si%, Mn%, and Al% satisfy Equation 8, and the steel structure is a structure of ferrite and bainite, and the strength is 590 N. High strength steel sheet excellent in hole expandability and ductility, characterized in that more than / mm2. -100 ≤ -300 [C%] + 105 [Si%]-95 [Mn%] + 233 [Al%]. (Eq. 8) The crystal grain size of the said steel structure WHEREIN: The hole expandability characterized by the presence of 80% or more of crystal grains whose ratio (ds / dl) of a short diameter (ds) and a long diameter (dl) is 0.1 or more. High strength steel sheet with excellent ductility. The high-strength steel sheet excellent in hole expandability and ductility according to claim 8, wherein in the ferrite grain of the steel structure, 80% or more of crystal grains having a particle diameter of 2 µm or more are present. Claim 1 or take Volume a steel of a composition described in 2 wherein in Ar ₃ is less than exit the rolling at least the rolling end temperature transformation point, and continuing to cooling to above 20 ℃ / sec cooling rate of 300 ℃, the steel structure A method for producing a high strength steel sheet, having excellent hole expandability and ductility, comprising a ferrite and martensite, and a structure containing residual austenite and having a strength of more than 590 N / mm 2. The first end of the rolling in the preceding claims, wherein a component end than the steel of the following composition Ar ₃ transformation point or rolling according to the temperature, and subsequently cooled to 650 ℃ to 750 ℃ in over 20 ℃ / sec cooling rate, and continue to the After cooling for 15 seconds or less at the temperature, it is cooled again and wound up at less than 300 DEG C, and the steel structure is a structure composed of ferrite and martensite, containing residual austenite, and having a strength of more than 590 N / mm 2. A method for producing a high strength steel sheet having excellent hole expandability and ductility, characterized by producing a steel sheet. The steel of the component composition of Claim 1 or 2 complete | finishes rolling at the rolling finishing temperature more than Ar3 transformation point, and then it cools by the cooling rate of 20 degree-C / sec or more, and it winds at ₃₀₀ degreeC or more and 600 degrees C or less. The high-strength steel sheet having excellent hole expandability and ductility, characterized in that the steel structure is made of ferrite and bainite, and the structure contains residual austenite, and a high strength steel sheet having a strength of more than 590 N / mm 2 is produced. Manufacturing method. The first end of the rolling in the preceding claims, wherein a component end than the steel of the following composition Ar ₃ transformation point or rolling according to the temperature, and subsequently cooled to 650 ℃ to 750 ℃ in over 20 ℃ / sec cooling rate, and continue to the After cooling for 15 seconds or less at the temperature, it was cooled again and wound up at 300 ° C. or higher and 600 ° C. or lower, and the steel structure was composed of ferrite and bainite, the structure containing residual austenite, and the strength was 590 N / mm 2. A method for producing a high strength steel sheet excellent in hole expandability and ductility, characterized by producing a high strength steel sheet that is in excess.

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