KR102485006B1 - High strength steel sheet having excellent workability and method for manufacturing the same - Google Patents

Abstract

The present invention relates to a steel sheet that can be used for automobile parts, etc., and relates to a steel sheet excellent in balance between strength and ductility, balance between strength and hole expandability, and yield ratio evaluation index, and a method for manufacturing the same.

Description

High strength steel sheet having excellent workability and method for manufacturing the same}

The present invention relates to a steel sheet that can be used for automobile parts, etc., and relates to a steel sheet having high strength and excellent workability and a method for manufacturing the same.

Recently, the automobile industry is paying attention to ways to promote weight reduction of materials to protect the global environment and at the same time to secure occupant safety. In order to meet these requirements for stability and light weight, the application of high-strength steel sheets is rapidly increasing. In general, it is known that the workability of the steel sheet decreases as the strength of the steel sheet is increased. Therefore, in the steel sheet for automobile parts, there is a demand for a steel sheet having high strength characteristics and excellent workability represented by ductility and hole expandability.

TRIP (Transformation Induced Plasticity) steel using the transformation-induced plasticity of retained austenite has a complex microstructure composed of ferrite, bainite, martensite, and retained austenite, so it has high strength characteristics and workability above a certain level. It is known.

As a technique for further improving the workability of steel sheets, methods of utilizing tempered martensite are disclosed in Patent Documents 1 and 2. Since tempered martensite made by tempering hard martensite is softened martensite, tempered martensite has a difference in strength from conventional untempered martensite (fresh martensite). Therefore, when fresh martensite is suppressed and tempered martensite is formed, workability may be increased.

However, with the techniques disclosed in Patent Documents 1 and 2, the balance of tensile strength and elongation (TS ² *EL ^1/2 ) does not satisfy the range of 3.0*10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ). This means that it is difficult to secure a steel sheet excellent in both strength and ductility.

On the other hand, as another technique for improving the workability of a steel sheet, a method of inducing formation of bainite through the addition of boron (B) is disclosed in Patent Document 3. When boron (B) is added, ferrite-pearlite transformation is suppressed and formation of bainite is induced, so that both strength and processability can be achieved.

However, in the technology disclosed in Patent Document 3, the balance between tensile strength and elongation of 3.0*10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ) and elongation (B _TE ), 6.0*10 ⁶ to 11.5*10 ⁶ (MPa ² % ^1/2 ) of tensile strength and hole expansion ratio (B _TH ) and yield ratio evaluation index (I _YR ) of 0.15 to 0.42 cannot be secured at the same time, which means that strength, hole expandability, ductility and yield ratio All of these means that it is difficult to secure a good steel plate.

That is, the balance of tensile strength and elongation (B _TE ), the balance of tensile strength and hole expansion (B _TH ), and the yield ratio evaluation index (I _YR ) do not all satisfy the demand for excellent steel sheets.

Korean Patent Publication No. 10-2006-0118602 Japanese Unexamined Patent Publication No. 2009-019258 Japanese Unexamined Patent Publication No. 2016-216808

According to one aspect of the present invention, a steel sheet excellent in balance between tensile strength and elongation, balance between tensile strength and hole expansion ratio, and yield ratio evaluation index by optimizing the composition and microstructure of the steel sheet and a method for manufacturing the same can be provided. there is.

The object of the present invention is not limited to the above. Additional tasks of the present invention are described throughout the specification, and those skilled in the art will have no difficulty in understanding the additional tasks of the present invention from the contents described in the specification of the present invention.

In the high-strength steel sheet with excellent workability according to one aspect of the present invention, by weight, C: 0.1 ~ 0.25%, Si: 0.01 ~ 1.5%, Mn: 1.0 ~ 4.0%, Al: 0.01 ~ 1.5%, P: 0.15% Hereinafter, S: 0.03% or less, N: 0.03% or less, B: 0.0005 to 0.005%, including the remaining Fe and unavoidable impurities, with a microstructure, bainite, tempered martensite, fresh martensite, retained austenite and Including other unavoidable organizations, the following [Relational Expression 1] to [Relational Expression 3] may be satisfied.

[Relationship 1]

0.03 ≤ [B] _FM /[B] _TM ≤ 0.55

In the above relational expression 1, [B] _FM is the content (wt%) of boron (B) contained in fresh martensite, and [B] _TM is the content (wt%) of boron (B) included in tempered martensite to be.

[Relationship 2]

V(1.2㎛, γ) / V(γ) ≥ 0.12

In the relational expression 2, V(1.2 μm, γ) is the retained austenite fraction (vol %) having an average grain size of 1.2 μm or more, and V(γ) is the retained austenite fraction (vol %) of the steel sheet.

[Relationship 3]

V(lath, γ) / V(γ) ≥ 0.5

In the relational expression 3, V(lath, γ) is the fraction of retained austenite in lath form (% by volume), and V(γ) is the fraction of retained austenite (% by volume) of the steel sheet.

The steel sheet may further include any one or more of (1) to (8) below, in terms of weight %.

(1) At least one of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%

(2) At least one of Cr: 0 to 3.0% and Mo: 0 to 3.0%

(3) At least one of Cu: 0 to 4.0% and Ni: 0 to 4.0%

(4) Ca: 0-0.05%, REM excluding Y: 0-0.05%, and Mg: 0-0.05% or more

(5) W: 0 to 0.5% and Zr: 0 to 0.5% at least one

(6) Sb: 0 to 0.5% and Sn: 0 to 0.5% at least one type

(7) Y: 0 to 0.2% and Hf: 0 to 0.2% at least one

(8) Co: 0~1.5%

The microstructure of the steel sheet, in volume fraction, is 10-30% bainite, 50-70% tempered martensite, 10-30% fresh martensite, 2-10% retained austenite, 5% or less (including 0%) of ferrite.

In the steel sheet, the balance between tensile strength and elongation (B _TE ) represented by [Relational Expression 4] below satisfies 3.0*10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ), and the following [Relational Expression 5 The balance of tensile strength and hole expansion ratio (B _TH ) expressed as ] satisfies 6.0*10 ⁶ to 11.5*10 ⁶ (MPa ² % ^1/2 ), and the yield ratio expressed by [Relational Expression 6] below is evaluated The index (I _YR ) may satisfy 0.15 to 0.42.

[Relationship 4]

B _TE = [tensile strength (TS, MPa)] ² * [elongation (El, %)] ^1/2

[Relationship 5]

B _TH = [tensile strength (TS, MPa)] ² * [hole expansion ratio (HER, %)] ^1/2

[Relationship 6]

I _YR = 1 - [yield ratio (YR)]

Method for manufacturing a high-strength steel sheet with excellent workability according to one aspect of the present invention, in weight%, C: 0.1 ~ 0.25%, Si: 0.01 ~ 1.5%, Mn: 1.0 ~ 4.0%, Al: 0.01 ~ 1.5%, P : 0.15% or less, S: 0.03% or less, N: 0.03% or less, B: 0.0005-0.005%, providing a cold-rolled steel sheet containing the remainder Fe and unavoidable impurities; The cold-rolled steel sheet is heated up to 700°C at an average heating rate of 5°C/s or more (first heating), and heated to a temperature range of Ac3 to 920°C at an average heating rate of 5°C/s or less (secondary heating). and then maintaining (primary maintenance) for 50 to 1200 seconds; Cooling (primary cooling) the steel sheet, which is primarily maintained, at an average cooling rate of 2 to 100 °C/s to a temperature range of 400 to 600 °C (primary cooling), and then maintaining (secondary holding) for 5 to 600 seconds; cooling (secondary cooling) the secondly maintained steel sheet to a temperature range of 300 to 500°C at an average cooling rate of 1 to 100°C/s and then maintaining (third holding) for 5 to 600 seconds; cooling (tertiary cooling) the tertiary maintained steel sheet to a temperature range of 200 to 400° C. at an average cooling rate of 2 to 100° C./s; Heating the tertiary cooled steel sheet to a temperature range of 350 to 550° C. at an average heating rate of 5 to 100° C./s (third heating) and then maintaining it for 50 seconds or longer (fourth holding); A step of cooling (quaternary cooling) the steel sheet maintained for the fourth time to room temperature at an average cooling rate of 1° C./s or more may be included.

The steel slab may further include any one or more of (1) to (8) below.

(1) At least one of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%

(2) At least one of Cr: 0 to 3.0% and Mo: 0 to 3.0%

(3) At least one of Cu: 0 to 4.0% and Ni: 0 to 4.0%

(4) Ca: 0-0.05%, REM excluding Y: 0-0.05%, and Mg: 0-0.05% or more

(5) W: 0 to 0.5% and Zr: 0 to 0.5% at least one

(6) Sb: 0 to 0.5% and Sn: 0 to 0.5% at least one type

(7) Y: 0 to 0.2% and Hf: 0 to 0.2% at least one

(8) Co: 0~1.5%

The cold-rolled steel sheet, heating the steel slab to 1000 ~ 1350 ℃; Finish hot rolling in the temperature range of 800 ~ 1000 ℃; Winding the hot-rolled steel sheet in a temperature range of 350 to 650 ° C; Pickling the rolled steel sheet; and cold-rolling the pickled steel sheet at a reduction ratio of 30 to 90%.

According to a preferred aspect of the present invention, it is possible to provide a steel sheet that can be suitably used for automobile parts and the like, and a method for manufacturing the same, since the balance between tensile strength and ductility, balance between tensile strength and hole expandability, and yield ratio evaluation index are excellent.

The present invention relates to a high-strength steel sheet with excellent workability and a method for manufacturing the same. Hereinafter, preferred embodiments of the present invention will be described. Embodiments of the present invention may be modified in various forms, and the scope of the present invention should not be construed as being limited to the embodiments described below. These embodiments are provided to those skilled in the art to further elaborate the present invention.

The inventors of the present invention are boron (B) addition type transformation induced plasticity (TRIP) steel containing bainite, tempered martensite, fresh martensite and retained austenite, tempered martensite, fresh martensite And the structure fraction of retained austenite is controlled within a certain range, the boron (B) content contained in tempered martensite and fresh martensite is controlled within a certain range, and the shape and size of retained austenite are controlled within a certain range In the case of control, it was recognized that it is possible to simultaneously secure an excellent balance of tensile strength and ductility, an excellent balance of tensile strength and hole expandability, and an excellent yield ratio evaluation index. By identifying this, a method for effectively achieving excellent strength, yield ratio, ductility and hole expandability was devised, and the present invention was reached.

Hereinafter, a high-strength steel sheet having excellent workability according to an aspect of the present invention will be described in more detail.

In the high-strength steel sheet with excellent workability according to one aspect of the present invention, by weight, C: 0.1 ~ 0.25%, Si: 0.01 ~ 1.5%, Mn: 1.0 ~ 4.0%, Al: 0.01 ~ 1.5%, P: 0.15% Hereinafter, S: 0.03% or less, N: 0.03% or less, B: 0.0005 to 0.005%, including the remaining Fe and unavoidable impurities, with a microstructure, bainite, tempered martensite, fresh martensite, retained austenite and Including other unavoidable organizations, the following [Relational Expression 1] to [Relational Expression 3] may be satisfied.

[Relationship 1]

0.03 ≤ [B] _FM /[B] _TM ≤ 0.55

In the above relational expression 1, [B] _FM is the content (wt%) of boron (B) contained in fresh martensite, and [B] _TM is the content (wt%) of boron (B) included in tempered martensite to be.

[Relationship 2]

V(1.2㎛, γ) / V(γ) ≥ 0.12

In the relational expression 2, V(1.2 μm, γ) is the retained austenite fraction (vol %) having an average grain size of 1.2 μm or more, and V(γ) is the retained austenite fraction (vol %) of the steel sheet.

[Relationship 3]

V(lath, γ) / V(γ) ≥ 0.5

In the relational expression 3, V(lath, γ) is the fraction of retained austenite in lath form (% by volume), and V(γ) is the fraction of retained austenite (% by volume) of the steel sheet.

Hereinafter, the steel composition of the present invention will be described in more detail. Hereinafter, % representing the content of each element is based on weight unless otherwise indicated.

In the high-strength steel sheet with excellent workability according to one aspect of the present invention, by weight, C: 0.1 ~ 0.25%, Si: 0.01 ~ 1.5%, Mn: 1.0 ~ 4.0%, Al: 0.01 ~ 1.5%, P: 0.15% Hereinafter, S: 0.03% or less, N: 0.03% or less, B: 0.0005 to 0.005%, the remainder includes Fe and unavoidable impurities. In addition, Ti: 0.5% or less (including 0%), Nb: 0.5% or less (including 0%), V: 0.5% or less (including 0%), Cr: 3.0% or less (including 0%), Mo: 3.0 % or less (including 0%), Cu: 4.0% or less (including 0%), Ni: 4.0% or less (including 0%), Ca: 0.05% or less (including 0%), REM excluding Y: 0.05% or less (including 0%), Mg: 0.05% or less (including 0%), W: 0.5% or less (including 0%), Zr: 0.5% or less (including 0%), Sb: 0.5% or less (including 0%), Sn: 0.5% or less (including 0%), Y: 0.2% or less (including 0%), Hf: 0.2% or less (including 0%), Co: 1.5% or less (including 0%) can do.

Carbon (C): 0.1 to 0.25%

Carbon (C) is an indispensable element for securing the strength of a steel sheet, and is also an element for stabilizing retained austenite contributing to the improvement of ductility of a steel sheet. Therefore, the present invention may include 0.1% or more of carbon (C) to achieve such an effect. Preferred carbon (C) content may be greater than 0.1%, may be greater than 0.11%, and may be greater than 0.12%. On the other hand, when the carbon (C) content exceeds a certain level, ductility and weldability may deteriorate due to an excessive increase in strength. Therefore, the present invention may limit the upper limit of the carbon (C) content to 0.25%. The carbon (C) content may be 0.24% or less, and a more preferable carbon content (C) may be 0.23% or less.

Silicon (Si): 0.01 to 1.5% or less

Silicon (Si) is an element that contributes to strength enhancement by solid solution strengthening, and is also an element that improves workability by homogenizing the structure. In addition, silicon (Si) is an element that contributes to the generation of retained austenite by suppressing the precipitation of cementite. Therefore, in the present invention, 0.01% or more of silicon (Si) may be added to achieve such an effect. A preferable silicon (Si) content may be 0.02% or more, and a more preferable silicon (Si) content may be 0.04% or more. However, if the silicon (Si) content exceeds a certain level, it may cause plating defects such as unplating in the plating process, as well as degrade the weldability of the steel sheet. can be limited to 1.5%. A preferable upper limit of the silicon (Si) content may be 1.48%, and a more preferable upper limit of the silicon (Si) content may be 1.46%.

Manganese (Mn): 1.0 to 4.0%

Manganese (Mn) is a useful element for increasing both strength and ductility. Therefore, in the present invention, 1.0% or more of manganese (Mn) may be added in order to achieve such an effect. A preferable lower limit of the manganese (Mn) content may be 1.2%, and a more preferable lower limit of the manganese (Mn) content may be 1.4%. On the other hand, when manganese (Mn) is excessively added, the bainite transformation time increases and the concentration of carbon (C) in austenite becomes insufficient, so that a desired austenite fraction cannot be secured. Therefore, the present invention may limit the upper limit of the manganese (Mn) content to 4.0%. The upper limit of the preferable manganese (Mn) content may be 3.9%.

Aluminum (Al): 0.01 to 1.5%

Aluminum (Al) is an element that acts as a deoxidizer by combining with oxygen in steel. In addition, aluminum (Al) is also an element that stabilizes retained austenite by suppressing cementite precipitation in the same way as silicon (Si). Therefore, in the present invention, 0.01% or more of aluminum (Al) may be added to achieve such an effect. A preferable aluminum (Al) content may be 0.03% or more, and a more preferable aluminum (Al) content may be 0.05% or more. On the other hand, when aluminum (Al) is excessively added, not only the inclusions of the steel sheet increase, but also the workability of the steel sheet can be deteriorated. In the present invention, the upper limit of the aluminum (Al) content can be limited to 1.5%. . The upper limit of the preferred aluminum (Al) content may be 1.48%.

Phosphorus (P): 0.15% or less (including 0%)

Phosphorus (P) is an element that is contained as an impurity and deteriorates impact toughness. Therefore, it is preferable to manage the phosphorus (P) content to 0.15% or less.

Sulfur (S): 0.03% or less (including 0%)

Sulfur (S) is an element that is contained as an impurity, forms MnS in the steel sheet, and deteriorates ductility. Therefore, the content of sulfur (S) is preferably 0.03% or less.

Nitrogen (N): 0.03% or less (including 0%)

Nitrogen (N) is an element that is contained as an impurity and causes cracks in the slab by creating nitride during continuous casting. Therefore, the content of nitrogen (N) is preferably 0.03% or less.

Boron (B): 0.0005 to 0.005%

Boron (B) is an element that increases strength by improving hardenability, and is also an element that suppresses nucleation of grain boundaries. In addition, since the present invention seeks to simultaneously secure an excellent tensile strength and elongation balance, an excellent tensile strength and hole expandability balance, and an excellent yield ratio evaluation index through boron (B) enrichment in tempered martensite, in the present invention boron ( B) must necessarily be added. Therefore, in the present invention, 0.0005% or more of boron (B) may be added for this effect. However, when boron (B) is added in excess of a certain level, it causes an excessive characteristic effect as well as an increase in manufacturing cost, so the upper limit of the boron (B) content may be limited to 0.005% in the present invention.

On the other hand, the steel sheet of the present invention has an alloy composition that may be additionally included in addition to the above-described alloy components, which will be described in detail below.

Titanium (Ti): 0 to 0.5%, niobium (Nb): 0 to 0.5%, and vanadium (V): 0 to 0.5% at least one of

Titanium (Ti), niobium (Nb), and vanadium (V) are elements that make precipitates and refine crystal grains, and are elements that also contribute to the improvement of strength and impact toughness of steel sheets. ), at least one of niobium (Nb) and vanadium (V) may be added. However, when the content of each of titanium (Ti), niobium (Nb), and vanadium (V) exceeds a certain level, excessive precipitates are formed, which not only reduces impact toughness, but also causes an increase in manufacturing cost, so the present invention Silver may limit the contents of titanium (Ti), niobium (Nb), and vanadium (V) to 0.5% or less, respectively.

Chromium (Cr): 0 to 3.0% and Molybdenum (Mo): 0 to 3.0% at least one

Chromium (Cr) and molybdenum (Mo) not only suppress austenite decomposition during alloying treatment, but also stabilize austenite in the same way as manganese (Mn), so the present invention provides chromium (Cr) and One or more of molybdenum (Mo) may be added. However, if the content of chromium (Cr) and molybdenum (Mo) exceeds a certain level, the bainite transformation time increases and the carbon (C) concentration in austenite becomes insufficient, thus securing the desired retained austenite fraction. Can not. Accordingly, the present invention may limit the contents of chromium (Cr) and molybdenum (Mo) to 3.0% or less, respectively.

Copper (Cu): 0 to 4.0% and Nickel (Ni): 0 to 4.0% at least one of

Copper (Cu) and nickel (Ni) are elements that stabilize austenite and inhibit corrosion. In addition, copper (Cu) and nickel (Ni) are also elements that are concentrated on the surface of the steel sheet and prevent hydrogen intrusion moving into the steel sheet, thereby suppressing delayed hydrogen destruction. Therefore, in the present invention, one or more of copper (Cu) and nickel (Ni) may be added for such an effect. However, when the contents of copper (Cu) and nickel (Ni) exceed a certain level, it causes not only excessive characteristic effects but also an increase in manufacturing cost. It can be limited to 4.0% or less.

Calcium (Ca): 0 to 0.05%, Magnesium (Mg): 0 to 0.05%, and rare earth elements (REM) excluding yttrium (Y): 0 to 0.05% at least one

Here, the rare earth element (REM) means scandium (Sc), yttrium (Y), and a lanthanide group element. Rare earth elements (REM), excluding calcium (Ca), magnesium (Mg), and yttrium (Y), are elements that contribute to improving the ductility of steel sheets by spheroidizing sulfides. At least one of rare earth elements (REM) other than magnesium (Mg) and yttrium (Y) may be added. However, when the content of rare earth elements (REM) other than calcium (Ca), magnesium (Mg), and yttrium (Y) exceeds a certain level, it causes excessive characteristic effects as well as an increase in manufacturing cost, so the present invention provides calcium ( Ca), magnesium (Mg), yttrium (Y) excluding rare earth elements (REM) content can be each limited to 0.05% or less.

At least one of Tungsten (W): 0 to 0.5% and Zirconium (Zr): 0 to 0.5%

Since tungsten (W) and zirconium (Zr) are elements that increase the strength of a steel sheet by improving hardenability, the present invention may add one or more of tungsten (W) and zirconium (Zr) for this effect. . However, when the content of tungsten (W) and zirconium (Zr) exceeds a certain level, it causes not only excessive characteristic effects but also an increase in manufacturing cost. % or less.

Antimony (Sb): 0 to 0.5% and Tin (Sn): 0 to 0.5% at least one

Since antimony (Sb) and tin (Sn) are elements that improve plating wettability and plating adhesion of a steel sheet, in the present invention, at least one of antimony (Sb) and tin (Sn) may be added for such an effect. However, when the content of antimony (Sb) and tin (Sn) exceeds a certain level, brittleness of the steel sheet increases and cracks may occur during hot or cold working. ) can be limited to 0.5% or less, respectively.

At least one of Yttrium (Y): 0 to 0.2% and Hafnium (Hf): 0 to 0.2%

Since yttrium (Y) and hafnium (Hf) are elements that improve the corrosion resistance of a steel sheet, the present invention may add one or more of yttrium (Y) and hafnium (Hf) for this effect. However, if the contents of yttrium (Y) and hafnium (Hf) exceed a certain level, the ductility of the steel sheet may be deteriorated. can be limited

Cobalt (Co): 0 to 1.5%

Since cobalt (Co) is an element that increases the TRIP effect by accelerating the bainite transformation, the present invention may add cobalt (Co) for this effect. However, if the content of cobalt (Co) exceeds a certain level, since weldability and ductility of the steel sheet may be deteriorated, the present invention may limit the content of cobalt (Co) to 1.5% or less.

A high-strength steel sheet having excellent workability according to an aspect of the present invention may include the remaining Fe and other unavoidable impurities in addition to the above components. However, since unintended impurities from raw materials or the surrounding environment may inevitably be mixed in the normal manufacturing process, it cannot be entirely excluded. Since these impurities can be known to anyone skilled in the art, all of them are not specifically mentioned in the present specification. In addition, additional addition of effective ingredients other than the above-mentioned ingredients is not entirely excluded.

The high-strength steel sheet having excellent workability according to one aspect of the present invention may include bainite, tempered martensite, fresh martensite, retained austenite, and other unavoidable structures as a microstructure.

Both untempered martensite (fresh martensite, FM) and tempered martensite (tempered martensite, TM) are microstructures that improve the strength of steel sheets. However, compared to tempered martensite, fresh martensite has a characteristic of lowering ductility and burring properties of the steel sheet. In addition, compared to tempered martensite, fresh martensite tends to lower the yield ratio of the steel sheet. This is because the microstructure of tempered martensite is softened by tempering heat treatment. Therefore, the balance of tensile strength and elongation (TS ² *EL ^1/2 ), the balance of tensile strength and hole expansion ratio (TS ² *HER ^1/2 ) and the yield ratio evaluation index (1-YR) It is preferable to control the tissue fraction of tempered martensite and fresh martensite in order to ensure. Balance of tensile strength and elongation of 3.0*10 ⁶ or more (TS ² *EL ^1/2 ), balance of tensile strength and hole expansion of 6.0*10 ⁶ or more (TS ² *HER ^1/2 ), and yield ratio of 0.42 or less In order to satisfy the index (1-YR), it is preferable to limit the fraction of tempered martensite to 50% by volume or more, and to limit the fraction of fresh martensite to 10% by volume or more. A more preferable tempered martensite fraction may be 52 vol% or more or 54 vol% or more, and a more preferable fresh martensite fraction may be 12 vol% or more. On the other hand, when tempered martensite or fresh martensite is excessively formed, ductility and burring properties are deteriorated, resulting in a balance between tensile strength and elongation of 3.0*10 ⁶ or more (TS ² *EL ^1/2 ), 6.0*10 ⁶ The balance of tensile strength and hole expansion ratio (TS ² *HER ^1/2 ) and the yield ratio evaluation index (1-YR) of 0.42 or less cannot be satisfied at the same time. Therefore, the present invention can limit the fraction of tempered martensite to 70% by volume or less, and limit the fraction of fresh martensite to 30% by volume or less. A more preferred fraction of tempered martensite may be 68 vol% or less or 65 vol% or less, and a more preferred fraction of fresh martensite may be 25 vol% or less.

Balance between tensile strength and elongation (TS ² *EL ^1/2 ), balance between tensile strength and hole expansion ratio (TS ² *HER ^1/2 ) and yield ratio evaluation index (1-YR) Optimization of the bainite fraction is necessary to secure . Balance of tensile strength and elongation of 3.0*10 ⁶ or more (TS ² *EL ^1/2 ), balance of tensile strength and hole expansion of 6.0*10 ⁶ or more (TS ² *HER ^1/2 ), and yield ratio of 0.42 or less In order to secure the index (1-YR), it is preferable to control the fraction of bainite to 10% by volume or more. A more preferred fraction of bainite may be 12 vol% or more or 14 vol% or more. On the other hand, excessive formation of bainite eventually causes a decrease in the fraction of tempered martensite, so the desired balance between tensile strength and elongation (TS ² *EL ^1/2 ), balance between tensile strength and hole expansion (TS ² *HER ^1/2 ) and the yield ratio evaluation index (1-YR), the fraction of bainite may be limited to 30% by volume or less. A preferred bainite fraction may be greater than or equal to 12% or greater than or equal to 14% by volume, or less than or equal to 28% or less than or equal to 26% by volume.

A steel sheet containing retained austenite has excellent ductility and workability due to transformation induced plasticity generated during transformation from austenite to martensite during processing. When the fraction of retained austenite is less than a certain level, the balance of tensile strength and elongation (TS ² *EL ^1/2 ) is less than 3.0 * 10 ⁶ (MPa ² % ^1/2 ), which is undesirable. On the other hand, when the fraction of retained austenite exceeds a certain level, local elongation may be lowered or spot weldability may be lowered. Therefore, in the present invention, the fraction of retained austenite may be limited to a range of 2 to 10% in order to obtain a steel sheet having an excellent balance between tensile strength and elongation (TS ² *EL ^1/2 ). A preferred retained austenite fraction may be greater than or equal to 3% by volume, or less than or equal to 8% by volume.

The steel sheet of the present invention may include ferrite, pearlite, martensite (Martensite Austenite Constituent, M-A) and the like as an unavoidable structure. Since the strength of the steel sheet may decrease when ferrite is excessively formed, the present invention may limit the fraction of ferrite to 5% by volume (including 0%) or less. In addition, when pearlite is excessively formed, the workability of the steel sheet may be deteriorated or the fraction of retained austenite may be reduced. Therefore, the present invention intends to limit the formation of pearlite as much as possible.

A high-strength steel sheet having excellent workability according to an aspect of the present invention may satisfy the following [Relational Expression 1] to [Relational Expression 3].

[Relationship 1]

0.03 ≤ [B] _FM /[B] _TM ≤ 0.55

In the above relational expression 1, [B] _FM is the content (wt%) of boron (B) contained in fresh martensite, and [B] _TM is the content (wt%) of boron (B) included in tempered martensite to be.

[Relationship 2]

V(1.2㎛, γ) / V(γ) ≥ 0.12

In the relational expression 2, V(1.2 μm, γ) is the retained austenite fraction (vol %) having an average grain size of 1.2 μm or more, and V(γ) is the retained austenite fraction (vol %) of the steel sheet.

[Relationship 3]

V(lath, γ) / V(γ) ≥ 0.5

In the relational expression 3, V(lath, γ) is the fraction of retained austenite in lath form (% by volume), and V(γ) is the fraction of retained austenite (% by volume) of the steel sheet.

The present invention secures the desired balance of tensile strength and elongation (TS ² *EL ^1/2 ), balance of tensile strength and hole expansion (TS ² *HER ^1/2 ), and yield ratio evaluation index (1-YR) In order to do this, not only the tissue fraction of tempered martensite, fresh martensite and retained austenite is controlled within a certain range, but also the boron (B) content ratio included in tempered martensite and fresh martensite is controlled within a certain range, , to control the ratio of retained austenite of a specific size, shape and type to the total retained austenite within a certain range.

The present invention, as shown in [Relational Expression 1], the content of boron (B) contained in fresh _martensite ([B] _FM , weight%) is controlled in the range of 0.03 to 0.55, so the balance of tensile strength and elongation (B _TE ) of 3.0*10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ), 6.0*10 ⁶ to A balance of tensile strength and hole expansion ratio (B _TH ) of 11.5*10 ⁶ (MPa ² % ^1/2 ) and a yield ratio evaluation index (I _YR ) of 0.15 to 0.42 can be secured at the same time.

The inventors of the present invention conducted in-depth research on methods for securing physical properties of boron (B)-added TRIP steel, and as a result, fresh martens for boron (B) content included in tempered martensite, although the theoretical basis has not been clearly identified. It has been noted that the desired physical properties of the present invention can be secured only when the ratio of the boron (B) content included in the site satisfies a certain range. In particular, it was confirmed that the yield ratio of the steel sheet showed a constant tendency according to the content ratio of boron (B) included in the tempered martensite and the fresh martensite. Therefore, since the present invention limits the ratio of the boron (B) content contained in the fresh martensite to the boron (B) content contained in the tempered martensite to the range of 0.03 to 0.55 as shown in [Relational Expression 1], the desired Balance between tensile strength and elongation (TS ² *EL ^1/2 ), balance between tensile strength and hole expansion ratio (TS ² *HER ^1/2 ), and yield ratio evaluation index (1-YR) can be secured.

In addition, the inventors of the present invention found that not only the fraction of retained austenite, but also the ratio of retained austenite of a specific size and shape to the total retained austenite is an important factor in securing strength and machinability.

As the ratio of retained austenite having an average grain size of 1.2 μm or more among the retained austenite increases, it can help to improve the workability of the steel sheet. Retained austenite with an average grain size of 1.2㎛ or more is heat treated at the bainite formation temperature to increase the average size of retained austenite, and the transformation driving force to martensite is relatively suppressed compared to retained austenite with an average grain size of 1.2㎛ or less. to be. Therefore, since the transformation of retained austenite having an average grain size of 1.2 μm or more is suppressed to martensite, the workability of the steel sheet can be more effectively improved when the ratio of retained austenite having an average grain size of 1.2 μm or more is above a certain level.

As the ratio of retained austenite in a lath form among retained austenite increases, it may be advantageous to improve workability of the steel sheet. Retained austenite is classified into residual austenite in a lath form formed between bainite phases and retained austenite in a block form formed in a portion without bainite phases. Since block-type retained austenite is additionally transformed into fresh martensite during the heat treatment process, workability of the steel sheet can be more effectively improved when the proportion of the residual austenite in the red form is higher than a certain level.

Retained austenite having an average grain size of 1.2 μm or more and retained austenite in a lath form are classified into retained austenite based on size and shape, respectively, and are mutually compatible concepts.

As shown in [Relational Expression 2], the present invention relates to the fraction of retained austenite having an average grain size of 1.2㎛ or more (V(1.2㎛, γ), Volume %) is controlled to be 0.12 or more, and the fraction of retained austenite in lath form relative to the fraction of total retained austenite (V(γ), volume %) included in the steel sheet as shown in [Relationship 3] Since the ratio of (V(lath, γ), volume %) is controlled to be 0.5 or more, the desired balance between tensile strength and elongation (TS ² *EL ^1/2 ) and balance between tensile strength and hole expansion (TS ² * HER ^1/2 ) can be secured effectively.

In the high-strength steel sheet having excellent workability according to one aspect of the present invention, the balance between tensile strength and elongation (B _TE ) expressed by [Relational Expression 4] below is 3.0*10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ) is satisfied, and the balance of tensile strength and hole expansion ratio (B _TH ) expressed by [Relational Expression 5] below satisfies 6.0*10 ⁶ to 11.5*10 ⁶ (MPa ² % ^1/2 ), and the following The yield ratio evaluation index (I _YR ) represented by [Relational Expression 6] may satisfy 0.15 to 0.42.

[Relationship 4]

B _TE = [tensile strength (TS, MPa)] ² * [elongation (El, %)] ^1/2

[Relationship 5]

B _TH = [tensile strength (TS, MPa)] ² * [hole expansion ratio (HER, %)] ^1/2

[Relationship 6]

I _YR = 1 - [yield ratio (YR)]

Hereinafter, an example of a method for manufacturing the steel sheet of the present invention will be described in detail.

In the method for manufacturing a high-strength steel sheet according to one aspect of the present invention, a cold-rolled steel sheet having a predetermined alloy composition is heated to 700° C. at an average heating rate of 5° C./s or more (primary heating), and 5° C./s or less Heating (secondary heating) to a temperature range of Ac3 to 920° C. at an average heating rate and then maintaining (primary maintenance) for 50 to 1200 seconds; Cooling (primary cooling) the steel sheet, which is primarily maintained, at an average cooling rate of 2 to 100 °C/s to a temperature range of 400 to 600 °C (primary cooling), and then maintaining (secondary holding) for 5 to 600 seconds; cooling (secondary cooling) the secondly maintained steel sheet to a temperature range of 300 to 500°C at an average cooling rate of 1 to 100°C/s and then maintaining (third holding) for 5 to 600 seconds; cooling (tertiary cooling) the tertiary maintained steel sheet to a temperature range of 200 to 400° C. at an average cooling rate of 2 to 100° C./s; Heating the tertiary cooled steel sheet to a temperature range of 350 to 550° C. at an average heating rate of 5 to 100° C./s (third heating) and then maintaining it for 50 seconds or longer (fourth holding); A step of cooling (quaternary cooling) the steel sheet maintained for the fourth time to room temperature at an average cooling rate of 1° C./s or more may be included.

The cold-rolled steel sheet, heating the steel slab having a predetermined alloy composition to 1000 ~ 1350 ℃; Finish hot rolling in the temperature range of 800 ~ 1000 ℃; Winding the hot-rolled steel sheet in a temperature range of 350 to 650 ° C; Pickling the rolled steel sheet; and cold-rolling the pickled steel sheet at a reduction ratio of 30 to 90%.

Preparation and heating of steel slabs

A steel slab having a predetermined alloy composition is prepared. Since the steel slab of the present invention has an alloy composition corresponding to the alloy composition of the above-described steel sheet, the description of the alloy composition of the steel slab is replaced with the description of the alloy composition of the above-described steel sheet.

The prepared steel slab may be heated to a certain temperature range, and the heating temperature of the steel slab at this time may be in the range of 1000 to 1350 ° C. If the heating temperature of the steel slab is less than 1000 ° C, it may be hot-rolled in a temperature range below the desired finish hot rolling temperature range, and if the heating temperature of the steel slab exceeds 1350 ° C, the steel reaches the melting point and melts. Possible.

hot rolled and coiled

The heated steel slab may be hot rolled to provide a hot rolled steel sheet. During hot rolling, the finish hot rolling temperature is preferably in the range of 800 to 1000°C. If the finish hot rolling temperature is less than 800 ° C, excessive rolling load may be a problem, and if the finish hot rolling temperature exceeds 1000 ° C, the crystal grains of the hot-rolled steel sheet are formed coarsely, which may cause a decrease in the physical properties of the final steel sheet. .

The hot-rolled steel sheet after hot rolling may be cooled at an average cooling rate of 10° C./s or more, and may be wound in a temperature range of 350 to 650° C. This is because when the coiling temperature is less than 350° C., the coiling is not easy, and when the coiling temperature exceeds 650° C., surface scale is formed to the inside of the hot-rolled steel sheet, which may make pickling difficult.

pickling and cold rolling

After uncoiling the wound hot-rolled coil, pickling may be performed to remove scale generated on the surface of the steel sheet, and cold rolling may be performed. In the present invention, pickling and cold rolling conditions are not particularly limited, but cold rolling is preferably carried out at a cumulative reduction of 30 to 90%. When the cumulative reduction ratio of cold rolling exceeds 90%, it may be difficult to perform cold rolling in a short time due to the high strength of the steel sheet.

The cold-rolled steel sheet may be manufactured as an uncoated cold-rolled steel sheet through an annealing heat treatment process, or may be manufactured as a coated steel sheet through a plating process to impart corrosion resistance. For plating, a plating method such as hot-dip galvanizing, electro-galvanizing, or hot-dip aluminum plating may be applied, and the method and type are not particularly limited.

annealing heat treatment

In the present invention, an annealing heat treatment process is performed in order to simultaneously secure strength and workability of a steel sheet.

The cold-rolled steel sheet was heated up to 700°C at an average heating rate of 5°C/s or more (first heating), and heated to a temperature range of Ac3 to 920°C at an average heating rate of 5°C/s or less (secondary heating). After that, it is maintained for 50 to 1200 seconds (primary maintenance).

When the average heating rate of the primary heating to 700 °C is less than 5 °C/s, bulk austenite is formed from ferrite and cementite generated during heating, and eventually fine tempered martensite and retained austenite are formed as the final structure. Cannot form knights. This makes it impossible to achieve the desired balance between tensile strength and elongation (TS ² *EL ^1/2 ) and balance between tensile strength and hole expansion (TS ² *HER ^1/2 ). In addition, when the secondary heating rate to the primary holding temperature exceeds 5° C./s, the transformation from cementite generated during heating to austenite is accelerated to form a large amount of bulk austenite, and the final structure is It is coarsened, and boron (B) may not be sufficiently enriched with tempered martensite. As a result, [B] _FM / [B] _TM exceeds 0.55, and the balance of tensile strength and elongation at the desired level (TS ² *EL ^1/2 ), balance between tensile strength and hole expansion (TS ² * HER ^1/2 ) and yield ratio evaluation index (I _YR ) cannot be implemented.

When the primary holding temperature is less than Ac3 (ideal range), more than 5% by volume of ferrite is formed, and accordingly, the balance between tensile strength and elongation (TS ² *EL ^1/2 ) and balance between tensile strength and hole expansion ( TS ² *HER ^1/2 ) may be lowered. In addition, when the primary holding time is less than 50 seconds, the physical properties of the steel sheet may be deteriorated because the structure cannot be sufficiently uniformed. The upper limits of the first holding temperature and the first holding time are not particularly limited, but in order to prevent a decrease in toughness due to grain coarsening, the first holding temperature is limited to 920 ° C or less and the first holding time is limited to 1200 seconds or less. it is desirable

After the 1st holding, it is cooled to the temperature range of 400 ~ 600℃ at the 1st cooling rate of 2℃/s or more (1st cooling), and then maintained for 5 seconds or longer (2nd holding) in the temperature range. . When the average cooling rate of the primary cooling is less than 2℃/s, the fraction of retained austenite becomes insufficient due to slow cooling, and accordingly, the balance between tensile strength and elongation (TS ² *EL ^1/2 ) and tensile strength of the steel sheet The balance (TS ² *HER ^1/2 ) of and hole expansion ratio may be lowered. The upper limit of the average cooling rate of primary cooling does not need to be particularly defined, but is preferably 100° C. or less. If the secondary holding temperature is less than 400℃, the balance between V(1.2㎛, γ) / V(γ) and tensile strength and hole expansion ratio (TS ² *HER ^1/2 ) of the steel sheet may be lowered due to the low heat treatment temperature. can On the other hand, when the secondary holding temperature exceeds 600°C, the retained austenite is insufficient, resulting in V(lath, γ) / V(γ) of the steel sheet, balance of tensile strength and elongation (TS ² *EL ^1/2 ), and The balance between tensile strength and hole expansion rate (TS ² *HER ^1/2 ) may be lowered. In addition, when the secondary holding time is less than 5 seconds, V (lath, γ) / V (γ), V (1.2㎛, γ) / V (γ) and tensile strength and hole expansion of the steel sheet due to insufficient heat treatment time The balance of rates (TS ² *HER ^1/2 ) may be lowered. The upper limit of the secondary holding time does not need to be specifically defined, but is preferably limited to 600 seconds or less.

After the secondary holding, it can be cooled to a temperature range of 300 to 500 ° C at an average cooling rate of 1 ° C / s or more (secondary cooling), and then maintained in the temperature range for more than 5 seconds (third holding). The upper limit of the average cooling rate of the secondary cooling does not need to be particularly defined, but is preferably 100° C./s or less. If the tertiary holding temperature is less than 300℃, the balance between V(1.2㎛, γ) / V(γ) and tensile strength and hole expansion rate (TS ² *HER ^1/2 ) of the steel sheet may be lowered due to the low heat treatment temperature. can On the other hand, when the 3rd holding temperature exceeds 500℃, retained austenite is insufficient, resulting in V(lath, γ) / V(γ) of the steel sheet, balance of tensile strength and elongation (TS ² *EL ^1/2 ), The balance between tensile strength and hole expansion rate (TS ² *HER ^1/2 ) may be lowered. In addition, when the tertiary holding time is less than 5 seconds, V(lath, γ) / V(γ), V(1.2㎛, γ) / V(γ), tensile strength and hole expansion rate of the steel sheet due to insufficient heat treatment time The balance (TS ² *HER ^1/2 ) of may be lowered. There is no need to specifically specify an upper limit for the tertiary holding time, but it is preferably limited to 600 seconds or less.

After the 3rd holding, it can be cooled (tertiary cooling) to the 1st cooling stop temperature of 200~400℃ at an average cooling rate of 2℃/s or more. When the average cooling rate of tertiary cooling is less than 2℃/s, the fraction of retained austenite becomes insufficient due to slow cooling, and accordingly, the balance between tensile strength and elongation of steel sheet (TS ² *EL ^1/2 ), tensile strength The balance (TS ² *HER ^1/2 ) of and hole expansion ratio may be lowered. The upper limit of the average cooling rate of the tertiary cooling does not need to be particularly defined, but is preferably 100° C./s or less. When the primary cooling stop temperature is less than 200℃, tempered martensite is excessively formed and retained austenite is insufficient, resulting in a balance between V(1.2㎛, γ) / V(γ), tensile strength and elongation of the steel sheet (TS ² * EL ^1/2 ) and balance between tensile strength and pore expansion rate (TS ² *HER ^1/2 ) may be lowered. On the other hand, when the primary cooling stop temperature exceeds 400 ° C, bainite is excessively formed and tempered martensite is insufficient, resulting in a balance between tensile strength and elongation (TS ² *EL ^1/2 ) and tensile strength and The hole expansion rate balance (TS ² *HER ^1/2 ) may be lowered.

After the tertiary cooling, it can be heated (third heating) to a temperature range of 350 to 550 ° C at a heating rate of 5 ° C. / s or more, and then maintained for 50 seconds or more (fourth maintenance). The upper limit of the average heating rate of the tertiary heating does not need to be particularly defined, but is preferably 100° C./s or less. When the 4th holding temperature is less than 350° C. or the 4th holding time is less than 50 seconds, tempered martensite is excessively formed, making it difficult to secure a fraction of retained austenite. As a result, V(1.2㎛, γ) / V(γ), the balance between tensile strength and elongation (TS ² *EL ^1/2 ), and the balance between tensile strength and pore expansion ratio (TS ² *HER ^1/2 ) decrease. It can be. When the 4th holding temperature exceeds 550°C or the 4th holding time exceeds 155,000 seconds, the fraction of retained austenite is insufficient, resulting in V(1.2㎛, γ) / V(γ), tensile strength and elongation of the steel sheet. The balance of (TS ² *EL ^1/2 ) and the balance of tensile strength and hole expansion ratio (TS ² *HER ^1/2 ) may be lowered.

After the 4th holding, it can be cooled (fourth cooling) to room temperature at an average cooling rate of 1°C/s or more.

The high-strength steel sheet with excellent processability manufactured by the above-described manufacturing method may include, as a microstructure, bainite, tempered martensite, fresh martensite, retained austenite, and other unavoidable structures, and as a preferred example, volume 10-30% bainite, 50-70% tempered martensite, 10-30% fresh martensite, 2-10% retained austenite, 5% or less (including 0%) ferrite. can include

The steel sheet manufactured by the above-described manufacturing method satisfies the balance between tensile strength and elongation (B _TE ) represented by the following [Relational Expression 4] of 3.0*10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ) And, the balance (B _TH ) of the tensile strength and the hole expansion ratio expressed by [Relational Expression 5] below satisfies 6.0 * 10 ⁶ to 11.5 * 10 ⁶ (MPa ² % ^1/2 ), and the following [Relational Expression 6 ] The yield ratio evaluation index (I _YR ) expressed as 0.15 to 0.42 may be satisfied.

[Relationship 4]

B _TE = [tensile strength (TS, MPa)] ² * [elongation (El, %)] ^1/2

[Relationship 5]

B _TH = [tensile strength (TS, MPa)] ² * [hole expansion ratio (HER, %)] ^1/2

[Relationship 6]

I _YR = 1 - [yield ratio (YR)]

Hereinafter, a high-strength steel sheet with excellent workability and a manufacturing method thereof according to an aspect of the present invention will be described in more detail through specific examples. It should be noted that the following examples are only for understanding of the present invention, and are not intended to specify the scope of the present invention. The scope of the present invention is determined by the matters described in the claims and the matters reasonably inferred therefrom.

(Example)

A steel slab having a thickness of 100 mm having an alloy composition shown in Table 1 (the remainder being Fe and unavoidable impurities) was prepared, heated at 1200 ° C, and then subjected to finish hot rolling at 900 ° C. Thereafter, it was cooled at an average cooling rate of 30° C./s and wound at the coiling temperature of Tables 2 and 3 to prepare a hot-rolled steel sheet having a thickness of 3 mm. Thereafter, after removing the surface scale by pickling, cold rolling was performed to a thickness of 1.5 mm.

Thereafter, heat treatment was performed under the annealing heat treatment conditions disclosed in Tables 2 to 7 to manufacture steel sheets.

The microstructure of the steel sheet thus prepared was observed and the results are shown in Tables 8 and 9. Among the microstructures, ferrite (F), bainite (B), tempered martensite (TM), fresh martensite (FM), and pearlite (P) were observed through SEM after nital etching of the polished specimen cross section. After nital etching, a structure without irregularities on the surface of the specimen was classified as ferrite, and a structure having a lamellar structure of cementite and ferrite was classified as pearlite. Since both bainite (B) and tempered martensite (TM) are observed in lath and block forms and are difficult to distinguish, the fraction of bainite and tempered martensite was calculated using an expansion curve after dilatation evaluation. That is, the value obtained by subtracting the fraction of bainite and tempered martensite calculated through the expansion curve from the fraction of bainite and tempered martensite measured by SEM observation was determined as the fraction of bainite. On the other hand, since fresh martensite (FM) and retained austenite (retained γ) are also not easy to distinguish, the fraction of retained austenite calculated by X-ray diffraction is subtracted from the fraction of martensite and retained austenite observed by the SEM. Values were determined as fractions of fresh martensite.

On the other hand, [B] _FM / [B] _TM , V (1.2㎛, γ) / V (γ), V (lath, γ) / V (γ), balance of tensile strength and elongation (TS ² *EL ^1/2 ), tensile strength and hole expansion ratio (TS ² *HER ^1/2 ), and yield ratio evaluation index (I _YR ) were measured and evaluated, and the results are shown in Tables 10 and 11.

The boron (B) content in fresh martensite ([B] _FM ) and the boron (B) content in tempered martensite ([B] _TM ) were determined by using EPMA (Electron Probe MicroAnalyser) for fresh martensite and tempered martensite. It was determined by the boron (B) concentration measured within. Retained austenite (V(1.2㎛, γ)) with an average grain size of 1.2㎛ or more and retained austenite in lath form (V(lath, γ)) are phase maps of EBSD (Electron Backscatter Diffraction) was measured using

Tensile strength (TS) and elongation (El) were evaluated through a tensile test, and the tensile strength (TS) and elongation were evaluated with test pieces taken in accordance with the JIS5 standard based on the 90° direction with respect to the rolling direction of the rolled sheet. (El) was measured. The hole expansion rate (HER) was evaluated through a hole expansion test, and after forming a punched hole of 10 mmΨ (die inner diameter 10.3 mm, clearance 12.5%), a conical punch with a 60° apex angle was used, and the burr of the punched hole was outside. It was inserted into the punching hole in the desired direction, and after pressing and expanding the area around the punching hole at a moving speed of 20 mm/min, it was calculated using [Relationship 7] below.

[Relationship 7]

Hole expansion rate (HER, %) = {(D - D ₀ ) / D ₀ } x 100

In the relational expression 7, D means the hole diameter (mm) when the crack penetrates the steel sheet along the thickness direction, and D ₀ means the initial hole diameter (mm).

steel grade Chemical composition (% by weight) C Si Mn P S Al N Cr Mo B Other A 0.13 0.53 2.04 0.010 0.0007 0.43 0.0028 0.0027 B 0.15 0.46 2.16 0.009 0.0012 0.52 0.0030 0.23 0.34 0.0023 C 0.16 0.63 2.32 0.007 0.0009 0.48 0.0031 0.57 0.0021 D 0.14 0.55 1.19 0.012 0.0010 0.93 0.0029 0.85 0.0024 E 0.15 1.46 2.52 0.007 0.0008 0.14 0.0033 0.0045 F 0.23 0.10 1.74 0.011 0.0011 1.47 0.0029 0.0041 G 0.17 0.34 2.26 0.012 0.0010 0.76 0.0031 0.0033 Ti: 0.04 H 0.12 0.39 2.40 0.010 0.0012 0.37 0.0030 0.0035 Nb: 0.04 I 0.20 0.42 2.63 0.007 0.0009 0.33 0.0029 0.0026 V: 0.05 J 0.14 0.25 1.85 0.010 0.0008 0.47 0.0025 0.0013 Ni: 0.34 K 0.19 0.51 2.37 0.008 0.0009 0.50 0.0031 0.0010 Cu: 0.35 L 0.16 0.77 2.15 0.010 0.0010 0.65 0.0032 0.0007 M 0.15 0.49 3.82 0.011 0.0011 0.59 0.0026 0.0008 Ca: 0.002 N 0.13 0.94 2.47 0.011 0.0010 0.54 0.0030 0.0034 REM: 0.001 O 0.20 0.65 2.32 0.009 0.0012 0.46 0.0028 0.0035 Mg: 0.001 P 0.14 0.57 2.19 0.010 0.0009 0.58 0.0026 0.0027 W: 0.13 Q 0.18 0.62 2.48 0.007 0.0012 0.43 0.0029 0.0029 Zr: 0.12 R 0.17 0.05 2.52 0.008 0.0008 1.48 0.0032 0.0023 Sb: 0.02 S 0.15 1.44 2.22 0.009 0.0009 0.04 0.0031 0.0025 Sn: 0.03 T 0.21 0.91 2.83 0.009 0.0007 0.45 0.0028 0.0021 Y: 0.03 U 0.14 0.72 2.91 0.010 0.0011 0.58 0.0030 0.0026 Hf: 0.01 V 0.17 0.64 2.60 0.007 0.0010 0.49 0.0028 0.0032 Co: 0.33 XA 0.08 0.56 2.52 0.008 0.0008 0.50 0.0027 0.0036 XB 0.28 0.53 2.36 0.008 0.0009 0.44 0.0029 0.0035 XC 0.14 0.003 2.44 0.011 0.0010 0.002 0.0032 0.0024 XD 0.12 1.53 2.63 0.012 0.0012 0.54 0.0030 0.0025 XE 0.17 0.50 2.74 0.010 0.0011 1.55 0.0031 0.0028 XF 0.18 0.46 0.83 0.011 0.0009 0.47 0.0029 0.0023 XG 0.15 0.62 4.18 0.008 0.0008 0.61 0.0027 0.0021 XH 0.20 0.51 2.62 0.009 0.0007 0.59 0.0032 3.20 0.0027 XI 0.16 0.48 2.50 0.007 0.0012 0.55 0.0029 3.19 0.0025 XJ 0.14 0.53 2.54 0.012 0.0010 0.48 0.0028 0.0003 XK 0.15 0.51 2.55 0.011 0.0008 0.46 0.0030 0.0053

Psalter
number steel grade hot rolled steel
winding temperature
(℃) 1st average
heating rate
(℃/s) 1st heating
stop temperature
(℃) 2nd average
heating rate
(℃/s) 1st maintenance
temperature range Primary
holding time
(s) One A 550 15 700 0.5 platform station 180 2 A 550 One 700 0.5 platform station 180 3 A 550 15 700 10 platform station 180 4 A 550 15 700 0.5 Lee Sang Station 180 5 A 550 15 700 0.5 platform station 180 6 A 550 15 700 0.5 platform station 180 7 A 550 15 700 0.5 platform station 180 8 A 550 15 700 0.5 platform station 180 9 A 550 15 700 0.5 platform station 180 10 A 550 15 700 0.5 platform station 180 11 A 550 15 700 0.5 platform station 180 12 A 550 15 700 0.5 platform station 180 13 A 550 15 700 0.5 platform station 180 14 A 550 15 700 0.5 platform station 180 15 A 550 15 700 0.5 platform station 180 16 A 550 15 700 0.5 platform station 180 17 A 550 15 700 0.5 platform station 180 18 A 550 15 700 0.5 platform station 180 19 B 500 15 700 0.5 platform station 180 20 C 500 15 700 0.5 platform station 180 21 D 500 15 700 0.5 platform station 180 22 E 450 15 700 0.5 platform station 180 23 F 450 15 700 0.5 platform station 180 24 G 450 15 700 0.5 platform station 180 25 H 500 15 700 0.5 platform station 180 26 I 550 15 700 0.5 platform station 180 27 J 400 15 700 0.5 platform station 180 28 K 600 15 700 0.5 platform station 180

Psalter
number steel grade hot rolled steel
winding temperature
(℃) 1st average
heating rate
(℃/s) 1st heating
stop temperature
(℃) 2nd average
heating rate
(℃/s) 1st maintenance
temperature range Primary
holding time
(s) 29 L 550 15 700 0.5 platform station 180 30 M 550 15 700 0.5 platform station 180 31 N 600 15 700 0.5 platform station 180 32 O 550 15 700 0.5 platform station 180 33 P 450 15 700 0.5 platform station 180 34 Q 550 15 700 0.5 platform station 180 35 R 400 15 700 0.5 platform station 180 36 S 500 15 700 0.5 platform station 180 37 T 500 15 700 0.5 platform station 180 38 U 500 15 700 0.5 platform station 180 39 V 500 15 700 0.5 platform station 180 40 XA 550 15 700 0.5 platform station 180 41 XB 550 15 700 0.5 platform station 180 42 XC 550 15 700 0.5 platform station 180 43 XD 550 15 700 0.5 platform station 180 44 XE 550 15 700 0.5 platform station 180 45 XF 500 15 700 0.5 platform station 180 46 XG 500 15 700 0.5 platform station 180 47 XH 500 15 700 0.5 platform station 180 48 XI 500 15 700 0.5 platform station 180 49 XJ 500 15 700 0.5 platform station 180 50 XK 500 15 700 0.5 platform station 180

Psalter
number steel grade 1st average
cooling rate
(℃/s) Secondary
maintain
Temperature
(℃) Secondary
maintain
time
(s) 2nd average
cooling rate
(℃/s) tertiary
maintain
Temperature
(℃) tertiary
maintain
time
(s) One A 20 500 40 10 400 40 2 A 20 500 40 10 400 40 3 A 20 500 40 10 400 40 4 A 20 500 40 10 400 40 5 A 0.5 500 40 10 400 40 6 A 20 370 40 10 400 40 7 A 20 630 40 10 400 40 8 A 20 500 2 10 400 40 9 A 20 500 40 10 270 40 10 A 20 550 40 10 520 40 11 A 20 500 40 10 400 2 12 A 20 500 40 10 400 40 13 A 20 500 40 10 400 40 14 A 20 500 40 10 450 40 15 A 20 500 40 10 400 40 16 A 20 500 40 10 400 40 17 A 20 500 40 10 400 40 18 A 20 500 40 10 400 40 19 B 20 500 40 10 400 40 20 C 20 500 40 10 400 40 21 D 20 500 40 10 400 40 22 E 20 500 40 10 350 40 23 F 20 450 40 10 400 40 24 G 20 450 40 10 350 40 25 H 20 550 40 10 400 40 26 I 20 550 40 10 450 40 27 J 20 500 40 10 400 40 28 K 20 500 40 10 450 40

Psalter
number steel grade 1st average
cooling rate
(℃/s) Secondary
maintain
Temperature
(℃) Secondary
maintain
time
(s) 2nd average
cooling rate
(℃/s) tertiary
maintain
Temperature
(℃) tertiary
maintain
time
(s) 29 L 20 500 40 10 400 40 30 M 20 500 40 10 400 40 31 N 20 450 40 10 400 40 32 O 20 550 40 10 400 40 33 P 20 500 40 10 350 40 34 Q 20 500 40 10 350 40 35 R 20 500 40 10 400 40 36 S 20 450 40 10 450 40 37 T 20 550 40 10 450 40 38 U 20 500 40 10 400 40 39 V 20 500 40 10 400 40 40 XA 20 500 40 10 400 40 41 XB 20 500 40 10 400 40 42 XC 20 500 40 10 400 40 43 XD 20 500 40 10 400 40 44 XE 20 500 40 10 400 40 45 XF 20 500 40 10 400 40 46 XG 20 500 40 10 400 40 47 XH 20 500 40 10 400 40 48 XI 20 500 40 10 400 40 49 XJ 20 500 40 10 400 40 50 XK 20 500 40 10 400 40

Psalter
number steel grade 3rd average
cooling rate
(℃/s) 1st cooling
stop temperature
(℃) 3rd average
heating rate
(℃/s) 4th maintenance
Temperature
(℃) 4th maintenance
time
(s) 4th average
cooling rate
(℃/s) One A 20 300 15 450 400 10 2 A 20 300 15 450 400 10 3 A 20 300 15 450 400 10 4 A 20 350 15 450 400 10 5 A 20 350 15 450 400 10 6 A 20 350 15 450 400 10 7 A 20 350 15 400 400 10 8 A 20 300 15 400 400 10 9 A 20 300 15 400 400 10 10 A 20 300 15 400 400 10 11 A 20 300 15 400 400 10 12 A 0.5 300 15 450 400 10 13 A 20 170 15 450 400 10 14 A 20 420 15 450 400 10 15 A 20 300 15 320 400 10 16 A 20 350 15 580 400 10 17 A 20 350 15 450 30 10 18 A 20 300 15 450 160,000 10 19 B 20 300 15 450 400 10 20 C 20 300 15 450 400 10 21 D 20 350 15 450 400 10 22 E 20 250 15 500 400 10 23 F 20 300 15 500 400 10 24 G 20 350 15 400 400 10 25 H 20 300 15 400 400 10 26 I 20 300 15 450 400 10 27 J 20 230 15 450 400 10 28 K 20 370 15 450 400 10

Psalter
number steel grade 3rd average
cooling rate
(℃/s) 1st cooling
stop temperature
(℃) 3rd average
heating rate
(℃/s) 4th maintenance
Temperature
(℃) 4th maintenance
time
(s) 4th average
cooling rate
(℃/s) 29 L 20 300 15 450 400 10 30 M 20 300 15 450 400 10 31 N 20 300 15 400 400 10 32 O 20 300 15 400 400 10 33 P 20 350 15 500 400 10 34 Q 20 250 15 500 400 10 35 R 20 350 15 400 400 10 36 S 20 230 15 400 400 10 37 T 20 370 15 450 400 10 38 U 20 300 15 450 400 10 39 V 20 300 15 450 400 10 40 XA 20 300 15 450 400 10 41 XB 20 300 15 450 400 10 42 XC 20 300 15 450 400 10 43 XD 20 350 15 450 400 10 44 XE 20 350 15 450 400 10 45 XF 20 300 15 400 400 10 46 XG 20 300 15 400 400 10 47 XH 20 350 15 400 400 10 48 XI 20 300 15 400 400 10 49 XJ 20 300 15 400 400 10 50 XK 20 300 15 400 400 10

Psalter
number steel grade F
(vol. %) B
(vol. %) TM
(vol.%) FM
(vol.%) P
(vol.%) γ
(vol.%) One A 0 23 57 14 0 6 2 A 0 29 44 26 0 One 3 A 0 17 57 15 4 7 4 A 15 13 54 14 0 4 5 A 0 24 58 17 0 One 6 A 0 20 57 18 0 5 7 A 0 19 63 17 0 One 8 A 0 20 61 15 0 4 9 A 0 21 60 16 0 3 10 A 0 23 59 17 0 One 11 A 0 22 58 15 0 5 12 A 0 19 62 18 0 One 13 A 0 14 73 12 0 One 14 A 0 32 46 16 0 6 15 A 0 15 72 12 0 One 16 A 0 17 67 15 0 One 17 A 0 13 73 13 0 One 18 A 0 19 65 15 0 One 19 B 0 18 61 16 0 5 20 C 0 22 57 14 0 7 21 D 0 19 58 17 0 6 22 E 0 17 61 14 0 8 23 F 0 18 59 17 0 6 24 G 0 20 60 16 0 4 25 H 0 23 57 15 0 5 26 I 0 21 58 14 0 7 27 J 0 17 62 15 0 6 28 K 0 18 57 17 0 8

number steel grade F
(vol.%) B
(vol. %) TM
(vol. %) FM
(vol.%) P
(vol.%) γ
(vol. %) 29 L 0 20 56 16 0 8 30 M 0 21 55 17 0 7 31 N 0 18 63 14 0 5 32 O 0 19 58 18 0 5 33 P 0 22 56 16 0 6 34 Q 0 21 57 14 0 8 35 R 0 18 62 15 0 5 36 S 0 19 54 20 0 7 37 T 0 22 57 17 0 4 38 U 0 20 58 15 0 7 39 V 0 19 59 14 0 8 40 XA 0 21 55 18 0 6 41 XB 0 15 40 32 0 13 42 XC 0 19 64 16 0 One 43 XD 0 13 51 32 0 4 44 XE 0 12 52 33 0 3 45 XF 0 15 61 13 10 One 46 XG 0 14 52 31 0 3 47 XH 0 11 53 32 0 4 48 XI 0 12 52 33 0 3 49 XJ 0 21 58 17 0 4 50 XK 0 19 63 15 0 3

number steel grade [B] _FM /
[B] _TM V(1.2㎛,γ)
/V(γ) V(lath,γ)
/V(γ) B _TE
(10 ⁶ MPa ² % ^1/2 ) _BTH
(10 ⁶ MPa ² % ^1/2 ) 1-YR One A 0.36 0.25 0.72 4.6 8.3 0.34 2 A 0.17 0.16 0.64 2.4 4.5 0.22 3 A 0.57 0.13 0.58 1.9 5.2 0.46 4 A 0.25 0.14 0.54 2.3 4.8 0.37 5 A 0.08 0.26 0.57 2.6 4.4 0.23 6 A 0.21 0.04 0.59 3.7 3.2 0.34 7 A 0.13 0.15 0.43 1.5 4.0 0.38 8 A 0.16 0.07 0.38 4.6 3.4 0.29 9 A 0.22 0.06 0.66 5.4 4.4 0.27 10 A 0.28 0.23 0.40 2.1 5.3 0.31 11 A 0.33 0.08 0.34 4.5 4.9 0.25 12 A 0.25 0.26 0.58 2.2 3.7 0.34 13 A 0.32 0.04 0.56 2.1 4.4 0.27 14 A 0.39 0.37 0.63 2.5 5.1 0.22 15 A 0.20 0.08 0.65 2.7 4.3 0.25 16 A 0.24 0.05 0.68 1.6 5.0 0.32 17 A 0.16 0.07 0.61 1.9 4.3 0.24 18 A 0.19 0.06 0.57 2.2 4.6 0.31 19 B 0.26 0.26 0.53 3.7 9.4 0.24 20 C 0.45 0.19 0.55 5.0 10.2 0.28 21 D 0.09 0.17 0.64 4.7 10.8 0.14 22 E 0.55 0.28 0.56 6.0 6.8 0.35 23 F 0.34 0.34 0.69 5.5 11.2 0.24 24 G 0.30 0.21 0.63 5.9 8.5 0.33 25 H 0.06 0.28 0.72 3.6 7.7 0.36 26 I 0.51 0.45 0.58 4.7 9.8 0.24 27 J 0.29 0.22 0.52 5.8 6.4 0.28 28 K 0.34 0.16 0.57 5.2 8.6 0.32

number steel grade [B] _FM /
[B] _TM V(1.2㎛,γ)
/V(γ) V(lath,γ)
/V(γ) B _TE
(10 ⁶ MPa ² % ^1/2 ) _BTH
(10 ⁶ MPa ² % ^1/2 ) 1-YR 29 L 0.29 0.17 0.64 5.2 10.8 0.35 30 M 0.36 0.23 0.56 3.4 9.7 0.23 31 N 0.28 0.24 0.59 4.8 8.9 0.27 32 O 0.12 0.22 0.60 5.5 9.0 0.25 33 P 0.33 0.15 0.73 4.5 8.1 0.30 34 Q 0.44 0.12 0.64 4.6 7.2 0.40 35 R 0.56 0.26 0.66 5.1 6.5 0.18 36 S 0.05 0.13 0.67 4.9 7.7 0.35 37 T 0.41 0.18 0.79 3.5 11.2 0.23 38 U 0.34 0.15 0.55 3.2 10.4 0.26 39 V 0.23 0.24 0.64 5.9 9.8 0.31 40 XA 0.22 0.20 0.53 2.2 4.5 0.25 41 XB 0.27 0.16 0.60 2.0 5.6 0.27 42 XC 0.18 0.13 0.54 1.6 5.3 0.33 43 XD 0.21 0.14 0.59 2.4 5.0 0.24 44 XE 0.27 0.19 0.58 1.8 5.6 0.30 45 XF 0.19 0.18 0.61 2.3 4.4 0.25 46 XG 0.20 0.16 0.59 2.2 5.2 0.28 47 XH 0.25 0.14 0.55 1.9 4.7 0.26 48 XI 0.16 0.15 0.53 2.3 4.1 0.23 49 XJ 0.58 0.21 0.62 3.4 6.5 0.44 50 XK 0.01 0.23 0.57 3.7 6.1 0.13

As shown in Tables 1 to 11, in the case of specimens satisfying the conditions presented in the present invention, both [Relational Expression 1] to [Relational Expression 3] are satisfied, and the balance between tensile strength and elongation (B _TE ) is 3.0* 10 ⁶ to 6.2*10 ⁶ (MPa ² % ^1/2 ) is satisfied, and the balance between tensile strength and hole expansion ratio (B _TH ) is 6.0*10 ⁶ to 11.5*10 ⁶ (MPa ² % ^1/2 ) It is satisfied, and it can be seen that the yield ratio evaluation index (I _YR ) satisfies 0.15 to 0.42.

Specimen 2 was carried out at a primary average heating rate of less than 5°C/s, and thus lacked tempered martensite and retained austenite. As a result, specimen 2 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

In specimen 3, when the second average heating rate was higher than 5° C./s, austenite was formed and boron (B) was not enriched in tempered martensite. As a result, specimen 3 had [B] _FM /[B] _TM greater than 0.55, yield ratio evaluation index (I _YR ) greater than 0.42, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , tensile strength and The hole expansion ratio balance (B _TH ) was less than 6.0*10 ⁶ .

In specimen 4, the primary holding temperature was carried out in an ideal region of less than Ac3, and the ferrite fraction exceeded. As a result, specimen 4 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Specimen 5 was carried out at a first average cooling rate of less than 2 ° C / s, and the retained austenite fraction was insufficient. As a result, specimen 5 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Specimen 6 was carried out at a secondary holding temperature of less than 400 ° C, and the heat treatment temperature was insufficient. As a result, specimen 6 had V(1.2㎛, γ) / V(γ) less than 0.12, and the balance between tensile strength and hole expansion ratio (B _TH ) was less than 6.0*10 ⁶ .

Specimen 7 was carried out at a secondary holding temperature of more than 600 ° C, and the retained austenite fraction was insufficient. As a result, specimen 7 had V(lath, γ) / V(γ) less than 0.5, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , and tensile strength and hole expansion ratio balance (B _TH ). It was less than 6.0*10 ⁶ .

In specimen 8, the secondary holding time was less than 5 seconds, and the heat treatment time was insufficient. As a result, for specimen 8, V(1.2㎛, γ) / V(γ) was less than 0.12, V(lath, γ) / V(γ) was less than 0.5, and the balance between tensile strength and hole expansion ratio (B _TH ) was 6.0. *10 was less than ⁶ .

Specimen 9 was carried out at a tertiary holding temperature of less than 300 ° C, and the heat treatment temperature was insufficient. As a result, specimen 9 had V(1.2㎛, γ) / V(γ) less than 0.12, and the balance between tensile strength and hole expansion ratio (B _TH ) was less than 6.0*10 ⁶ .

Specimen 10 was carried out at a tertiary holding temperature of more than 500 ° C, and the retained austenite fraction was insufficient. As a result, specimen 10 had V(lath, γ) / V(γ) less than 0.5, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , and tensile strength and hole expansion ratio balance (B _TH ). It was less than 6.0*10 ⁶ .

Specimen 11 had a tertiary holding time of less than 5 seconds, and the heat treatment time was insufficient. As a result, for specimen 11, V(1.2㎛, γ) / V(γ) was less than 0.12, V(lath, γ) / V(γ) was less than 0.5, and the balance between tensile strength and hole expansion ratio (B _TH ) was 6.0. *10 was less than ⁶ .

Specimen 12 was carried out at a tertiary average cooling rate of less than 2 ° C / s, and the retained austenite fraction was insufficient. The balance between tensile strength and elongation (B _TE ) was less than 3.0*10 ⁶ , and the balance between tensile strength and hole expansion ratio (B _TH ) was less than 6.0*10 ⁶ .

Specimen 13 was carried out at a first cooling stop temperature of less than 200 ° C, so the tempered martensite fraction was exceeded and the retained austenite fraction was insufficient. As a result, specimen 13 had V(1.2㎛, γ) / V(γ) less than 0.12, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , tensile strength and hole expansion ratio balance (B _TH ) was less than 6.0*10 ⁶ .

Specimen 14 was carried out at a first cooling stop temperature of more than 400 ° C., so that the bainite fraction was exceeded and the tempered martensite fraction was insufficient. As a result, specimen 14 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Specimen 15 was carried out at a 4th holding temperature of less than 350 ° C, so the tempered martensite fraction was exceeded and the retained austenite fraction was insufficient. As a result, specimen 15 had V(1.2㎛, γ) / V(γ) less than 0.12, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , tensile strength and hole expansion ratio balance (B _TH ) was less than 6.0*10 ⁶ .

Specimen 16 was carried out at the 4th holding temperature above 550 ° C, and the retained austenite fraction was insufficient. As a result, specimen 16 had V(1.2㎛, γ) / V(γ) less than 0.12, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , tensile strength and hole expansion ratio balance (B _TH ) was less than 6.0*10 ⁶ .

In specimen 17, the 4th holding time was less than 50 s, so the tempered martensite fraction was exceeded and the retained austenite fraction was insufficient. As a result, specimen 17 had V(1.2㎛, γ) / V(γ) less than 0.12, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , tensile strength and hole expansion ratio balance (B _TH ) was less than 6.0*10 ⁶ .

Specimen 18 was carried out at the 4th holding time exceeding 155000 s, and the retained austenite fraction was insufficient. As a result, specimen 18 had silver V(1.2㎛, γ) / V(γ) less than 0.12, tensile strength and elongation balance (B _TE ) less than 3.0*10 ⁶ , tensile strength and hole expansion rate balance (B _TH ) was less than 6.0*10 ⁶ .

Specimen 40 had a low carbon (C) content, so the balance between tensile strength and elongation (B _TE ) was less than 3.0*10 ⁶ , and the balance between tensile strength and hole expansion (B _TH ) was less than 6.0*10 ⁶ .

In specimen 41, the tempered martensite fraction was insufficient due to the high carbon (C) content, the fresh martensite fraction exceeded, and the retained austenite fraction exceeded. As a result, specimen 41 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Sample 42 had a low content of silicon (Si) and lacked a retained austenite fraction. As a result, specimen 42 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Sample 43 had a high silicon (Si) content and exceeded the fresh martensite fraction. As a result, specimen 43 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Sample 44 had a high aluminum (Al) content and exceeded the fresh martensite fraction. As a result, specimen 44 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Specimen 45 had a low content of manganese (Mn) and lacked the retained austenite fraction due to the formation of pearlite. As a result, specimen 45 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Sample 46 had a high manganese (Mn) content and exceeded the fresh martensite fraction. As a result, specimen 46 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Sample 47 had a high chromium (Cr) content, and the fresh martensite fraction was exceeded. As a result, specimen 47 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Sample 48 had a high molybdenum (Mo) content and exceeded the fresh martensite fraction. As a result, specimen 48 had a balance of tensile strength and elongation (B _TE ) of less than 3.0*10 ⁶ and a balance of tensile strength and hole expansion (B _TH ) of less than 6.0*10 ⁶ .

Specimen 49 was low in boron (B) content, so boron (B) was not enriched in tempered martensite. As a result, for specimen 49, [B] _FM /[B] _TM exceeded 0.55 and yield ratio evaluation index (I _YR ) exceeded 0.42.

Specimen 50 had a high boron (B) content, so boron (B) was excessively enriched in tempered martensite. As a result, specimen 50 had [B] _FM /[B] _TM less than 0.03 and yield ratio evaluation index (I _YR ) less than 0.15.

Although the present invention has been described in detail through examples above, other types of embodiments are also possible. Therefore, the spirit and scope of the claims set forth below are not limited to the embodiments.

Claims (7)

In weight percent, C: 0.1 to 0.25%, Si: 0.01 to 1.5%, Mn: 1.0 to 4.0%, Al: 0.01 to 1.5%, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, B: 0.0005 to 0.005%, including the remainder Fe and unavoidable impurities,
The microstructure includes bainite, tempered martensite, fresh martensite, retained austenite and other unavoidable structures,
[Relational Expression 1] to [Relational Expression 3] below are satisfied,
The balance of tensile strength and elongation (B _TE ) represented by [Relational Expression 4] below satisfies 3.0 * 10 ⁶ to 6.2 * 10 ⁶ (MPa ² % ^1/2 ), and is represented by [Relational Expression 5] below The balance of tensile strength and hole expansion ratio (B _TH ) satisfies 6.0*10 ⁶ to 11.5*10 ⁶ (MPa ² % ^1/2 ), and the yield ratio evaluation index (I _YR expressed by [Relational Expression 6] below ) satisfies 0.15 to 0.42, high-strength steel sheet with excellent workability.
[Relationship 1]
0.03 ≤ [B] _FM /[B] _TM ≤ 0.55
In the above relational expression 1, [B] _FM is the content (wt%) of boron (B) contained in fresh martensite, and [B] _TM is the content (wt%) of boron (B) included in tempered martensite to be.
[Relationship 2]
V(1.2㎛, γ) / V(γ) ≥ 0.12
In the relational expression 2, V(1.2 μm, γ) is the retained austenite fraction (vol %) having an average grain size of 1.2 μm or more, and V(γ) is the retained austenite fraction (vol %) of the steel sheet.
[Relationship 3]
V(lath, γ) / V(γ) ≥ 0.5
In the relational expression 3, V(lath, γ) is the fraction of retained austenite in lath form (% by volume), and V(γ) is the fraction of retained austenite (% by volume) of the steel sheet.
[Relationship 4]
B _TE = [tensile strength (TS, MPa)] ² * [elongation (El, %)] ^1/2
[Relationship 5]
B _TH = [tensile strength (TS, MPa)] ² * [hole expansion ratio (HER, %)] ^1/2
[Relationship 6]
I _YR = 1 - [yield ratio (YR)]
According to claim 1,
The steel sheet, in weight%, further comprises any one or more of (1) to (8) below, high-strength steel sheet excellent in workability.
(1) At least one of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%
(2) At least one of Cr: 0 to 3.0% and Mo: 0 to 3.0%
(3) At least one of Cu: 0 to 4.0% and Ni: 0 to 4.0%
(4) Ca: 0-0.05%, REM excluding Y: 0-0.05%, and Mg: 0-0.05% or more
(5) W: 0 to 0.5% and Zr: 0 to 0.5% at least one
(6) Sb: 0 to 0.5% and Sn: 0 to 0.5% at least one type
(7) Y: 0 to 0.2% and Hf: 0 to 0.2% at least one
(8) Co: 0~1.5%
According to claim 1,
The microstructure of the steel sheet, in volume fraction, is 10-30% bainite, 50-70% tempered martensite, 10-30% fresh martensite, 2-10% retained austenite, 5% or less A high-strength steel sheet with excellent workability, containing ferrite (including 0%).
delete In weight percent, C: 0.1 to 0.25%, Si: 0.01 to 1.5%, Mn: 1.0 to 4.0%, Al: 0.01 to 1.5%, P: 0.15% or less, S: 0.03% or less, N: 0.03% or less, B: providing a cold-rolled steel sheet containing 0.0005 to 0.005%, the remainder Fe and unavoidable impurities;
The cold-rolled steel sheet is heated up to 700°C at an average heating rate of 5°C/s or more (first heating), and heated to a temperature range of Ac3 to 920°C at an average heating rate of 5°C/s or less (secondary heating). and then maintaining (primary maintenance) for 50 to 1200 seconds;
Cooling (primary cooling) the steel sheet, which is primarily maintained, at an average cooling rate of 2 to 100 °C/s to a temperature range of 400 to 600 °C (primary cooling), and then maintaining (secondary holding) for 5 to 600 seconds;
cooling (secondary cooling) the secondly maintained steel sheet to a temperature range of 300 to 500°C at an average cooling rate of 1 to 100°C/s and then maintaining (third holding) for 5 to 600 seconds;
cooling (tertiary cooling) the tertiary maintained steel sheet to a temperature range of 200 to 400° C. at an average cooling rate of 2 to 100° C./s;
Heating the tertiary cooled steel sheet to a temperature range of 350 to 550° C. at an average heating rate of 5 to 100° C./s (third heating) and then holding for 50 to 155,000 seconds (fourth holding); and
A method for producing a high-strength steel sheet with excellent workability, comprising the step of cooling (quaternary cooling) the fourth-maintained steel sheet to room temperature at an average cooling rate of 1 ° C. / s or more.
According to claim 5,
The cold-rolled steel sheet further comprises any one or more of the following (1) to (8), a method for producing a high-strength steel sheet with excellent workability.
(1) At least one of Ti: 0 to 0.5%, Nb: 0 to 0.5%, and V: 0 to 0.5%
(2) At least one of Cr: 0 to 3.0% and Mo: 0 to 3.0%
(3) At least one of Cu: 0 to 4.0% and Ni: 0 to 4.0%
(4) Ca: 0-0.05%, REM excluding Y: 0-0.05%, and Mg: 0-0.05% or more
(5) W: 0 to 0.5% and Zr: 0 to 0.5% at least one
(6) Sb: 0 to 0.5% and Sn: 0 to 0.5% at least one type
(7) Y: 0 to 0.2% and Hf: 0 to 0.2% at least one
(8) Co: 0~1.5%
According to claim 5,
The cold rolled steel sheet,
heating the steel slab to 1000-1350°C;
Finish hot rolling in the temperature range of 800 ~ 1000 ℃;
Winding the hot-rolled steel sheet in a temperature range of 350 to 650 ° C;
Pickling the rolled steel sheet; and
Cold-rolling the pickled steel sheet at a reduction rate of 30 to 90%; method for producing a high-strength steel sheet with excellent workability provided through.