HOT-ROLLED FERRITIC STAINLESS STEEL SHEET HAVING EXCELLENT FORMABILITY AND METHOD FOR MANUFACTURING SAME

Abstract

The present invention pertains to a hot-rolled ferritic stainless steel sheet having excellent formability, which has an R-bar value of at least 1.08 and satisfies TS/YS≤1.5 representing the ratio of tensile strength (TS) to yield strength (YS) after a steel, containing 0.001-0.1% of C, 10.0-14.0% of Cr, 0.001-0.5% of Ti, 0.001-0.5% of Nb, 0.001-1.5% of Ni, 0.001-1.5% of Mn, 0.001-1.0% of Cu, 0.001-2.0% of Si, 0.001-0.1% of N, and 0.1% or less of Al, with the remainder comprising Fe and inevitable impurities, is hot-rolled and then pre-rolled at a reduction ratio of 30% or more.

Description

TECHNICAL FIELD

The disclosure relates to a hot-rolled ferritic stainless steel sheet having excellent formability and manufacturing method thereof.

BACKGROUND ART

Cold-rolled ferritic stainless steel products have excellent high-temperature characteristics such as thermal expansion coefficient and thermal fatigue, are robust to stress corrosion cracking, and also have excellent high-temperature strength. Based on these characteristics, the ferritic stainless steel is applied to vehicle exhaust systems, household tools, structures, home appliances, elevators, etc. To expand the application ranges of the ferritic stainless steel, it is important to secure formability. As the deformation mechanism of the ferritic stainless steel causes transformation according to generation and movement of dislocations unlike an austenitic stainless steel, which has high processability according to plastic induced transformation, the ferritic stainless steel is characterized by having formability changing by increasing an amount of rolling to activate generation and movement of dislocations or controlling impurities that interfere the movement of dislocations. Although many researches have made efforts to increase formability of the ferritic stainless steel, the ferritic stainless steel has problem being vulnerable to stretching forming. Furthermore, hot-rolled materials have a low strain rate, which leads to difficulty in generating dislocations, so even with the same thickness, have difficulty in securing as much formability as a cold-rolled annealed material, and thus, there are limits to applying the hot-rolled material to a product that requires high formability.

DISCLOSURE

Technical Problem

To solve the above problem, an objective of the disclosure is to manufacture a hot-rolled stainless steel sheet that exhibits similar formability to cold-rolled materials despite being a hot-rolled material by rolling a hot-rolled steel sheet at a certain reduction rate to control a banded structure formed in the hot-rolled material before annealing the hot-rolled steel sheet, and additionally activating generation of dislocations to refine crystal grains and simultaneously, increase formability after hot annealing.

Technical Solution

According to an embodiment of the disclosure, a hot-rolled ferritic stainless steel sheet with excellent formability satisfies a value of R-bar being 1.08 or more and a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5, after hot rolling a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.1% of N, 0.1% or less of Al and the remainder having Fe and unavoidable impurities and pre-rolling the steel at a reduction rate of 30% or more.

According to another embodiment of the disclosure, a method of manufacturing a hot-rolled ferritic stainless steel sheet with excellent formability comprises manufacturing a slab by continuously casting a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.10% of N, 0.10% or less of Al and the remainder having Fe and unavoidable impurities; reheating the manufactured slab; hot rolling the reheated slab; performing pre-rolling at a reduction rate of 30% or more to satisfy a value of R-bar being 1.08 or more and a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5; and performing hot annealing.

Advantageous Effects

According to the disclosure, a hot-rolled stainless steel sheet that exhibits similar formability to cold-rolled materials despite being a hot-rolled material by controlling a banded structure formed in the hot-rolled material in a case of rolling the hot-rolled steel sheet at a reduction rate of 30% or more before annealing the hot-rolled steel sheet, and additionally activating generation of dislocations to refine crystal grains and simultaneously, increase formability after hot annealing.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 illustrates a microstructure of embodiment 1 (ferritic stainless steel 35% pre-rolling annealed material).

FIG. 2 illustrates a microstructure of embodiment 2 (ferritic stainless steel 50% pre-rolling annealed material).

FIG. 3 illustrates a microstructure of comparative example 1 (hot-rolled annealed material (2.0t) of ferritic stainless steel).

FIG. 4 illustrates a microstructure of comparative example 2 (ordinary cold annealed material of ferritic stainless steel).

BEST MODE

According to an embodiment of the disclosure, a hot-rolled ferritic stainless steel sheet with excellent formability satisfies a value of R-bar being 1.08 or more and a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5, after hot rolling a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.1% of N, 0.1% or less of Al and the remainder having Fe and unavoidable impurities and pre-rolling the steel at a reduction rate of 30% or more.

[Modes]

Various methods have thus far been examined to enhance formality of ferritic stainless steel. In general, there is a method of facilitating recrystallization by keeping the hot rolling reheating temperature low or rolling at a high reduction rate in a rear stage of rough rolling to activate the introduction of dislocations, but there is a clear limit to actually applying the method because the method makes it difficult to form surface oxidation scales at a low reheating temperature when applied in actual production, causing various surface defects including sticking defects or in severe cases, causing a problem with fracture due to cracks.

To overcome the shortcomings, the disclosure provides a method of manufacturing a ferritic stainless steel that exhibits similar formability to cold-rolled materials by rolling a hot-rolled steel sheet at a certain reduction rate to control a banded structure formed in the hot-rolled material before annealing the hot-rolled steel sheet, and additionally activating generation of dislocations to refine crystal grains and simultaneously, increase formability after hot annealing.

[Hot-Rolled Ferritic Stainless Steel Sheet]

According to an embodiment of the disclosure, a hot-rolled ferritic stainless steel sheet with excellent formability satisfies a value of R-bar being 1.08 or more and a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5, after hot rolling a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.1% of N, 0.1% or less of Al and the remainder having Fe and unavoidable impurities and pre-rolling the steel at a reduction rate of 30% or more, wherein a reduction rate of pre-rolling may be 35% or more.

Furthermore, according to another embodiment of the disclosure, a hot-rolled ferritic stainless steel sheet with excellent formability may have a ferrite crystal grain size of 60 μm or less when the crystal grain size is measured in an electron backscattering diffraction (EBSD) analysis method with intergranular misorientation ranging from 15° to 180°.

A unit of wt % will now be used unless otherwise mentioned. The term “include (or including)” or “comprise (or comprising)” is inclusive or open-ended and does not exclude additional, unrecited elements or method steps, unless otherwise mentioned.

(Ranges of Composition)

C: 0.001˜0.1%

When there is a large amount of carbon, strength is enhanced but processability is reduced. In order to obtain sufficient strength, 0.001% or more of carbon needs to be contained, but when the carbon exceeds 0.10%, it leads to reduction in processability.

Cr: 10.0˜14.0%

The amount of chrome is desirably 10.0 to 14.0%. Chrome is an important element to be added to secure corrosion resistance of the stainless steel, and in the disclosure, 10.0% or more of chrome is added to increase corrosion resistance. When chrome C exceeds 14.0%, it causes hot rolling sticking defects, so 14.0% or less is desirable.

Ti: 0.001˜0.5%

The amount of titanium is desirably 0.001 to 0.5%. When the amount of titanium is less than 0.001%, the amount of TiN crystallization decreases, which lowers the equiaxed crystal ratio of the slab, and the dissolved C and N elements increase, causing a decrease in elongation rate, and when it exceeds 0.5%, Ti-based oxides increase, which deteriorates processability.

Nb: 0.001˜0.5%

The amount of niobium is desirably 0.001 to 0.5%. Niobium preferentially combines with carbon and nitrogen to form precipitates that suppress the deterioration of corrosion resistance, but when added in excess, it causes poor appearance and reduced toughness due to the inclusions and increases raw material costs, so the content of the niobium is limited to 0.001 to 0.5%.

Ni: 0.001˜1.5%

The amount of nickel is desirably 0.001 to 1.5%. Nickel is an element that enhances corrosion resistance, but when added in a large amount, it may not only harden but also cause stress corrosion cracking, so it is desirable for nickel to be 1.5% or less.

Mn: 0.001˜1.5%

The amount of manganese is desirably 0.001 to 1.5%. Manganese has an effect of increasing the strength of steel but when contained excessively, generation of Mn-based fume rapidly increases, which deteriorates weldability, and ductility of the steel deteriorates due to excessive formation of MnS precipitates, so manganese is contained at 1.5% or less.

Cu: 0.001˜1.0%

The amount of copper is desirably 1.0% or less. Copper has an effect of enhancing corrosion resistance, but when it is over 1.0%, it deteriorates processability.

Si: 0.001˜2.0%

Silicon is an element that is added for deoxidization of molten steel and ferrite stabilization during steelmaking and is desirably 0.001% or more, but when the content is excessive, it causes hardening of the material and thus, deteriorates ductility of the steel, so the content is limited to 2.0% or less.

N: 0.001˜0.1%

The amount of nitrogen is desirably 0.001 to 0.1%. Like carbon, nitrogen has an effect of increasing the strength of material. When the amount of nitrogen is less than 0.001%, TiN crystallization decreases and thus, the equiaxed crystal ratio of the slab is lowered, and when it exceeds 0.1%, impurities in the material increase, causing a decrease in elongation rate.

Al: 0.1% or less

The amount of aluminum is desirably 0.1% or less. When the amount of aluminum exceeds 0.1%, impurities in the material increase and the elongation rate is lowered.

[Method of Manufacturing Hot-Rolled Ferritic Stainless Steel Sheet]

According to an embodiment of the disclosure, a method of manufacturing a hot-rolled ferritic stainless steel sheet with excellent formability comprises manufacturing a slab by continuously casting a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.1% of N, 0.1% or less of Al and the remainder having Fe and unavoidable impurities; reheating the manufactured slab; hot rolling the reheated slab; performing pre-rolling at a reduction rate of 30% or more to satisfy a value of R-bar being 1.08 or more and a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5; and

performing hot annealing.

Reheating temperature of hot rolling ranges from 1100° C. to 1280° C. When the slab is reheated at a temperature of more than 1280° C. or more, a coarse banded structure is more likely to remain, causing deterioration of formability, and when the slab is reheated at less than 1100° C., the rolling load increases during hot rolling, which may be likely to reduce productivity.

Embodiments of the disclosure will now be described in more detail.

The following embodiments are provided to deliver the idea of the disclosure to those of ordinary skill in the art, but the disclosure is not limited to the embodiments and may be implemented in other forms.

EMBODIMENTS

For a hot-rolled ferritic stainless steel sheet obtained by manufacturing a slab by continuously casting, reheating the slab, performing hot rolling, performing pre-rolling with a hot rolling thickness of 2.0 to 5.0t, a thickness of 2.0t after the pre-rolling, and a reduction rate of 0 to 50%, and performing hot annealing, grain size, R values (R₀, R₄₅, R₉₀, and R-bar), yield strength, tensile strength, TS/YS and an elongation rate were measured.

TABLE 1
section (wt %)	C	Si	Mn	Cr	Ni	Cu	Ti	Nb	N	A
Example 1	0.007	0.446	0.26	11.12	0.075	0.013	0.19	0.002	0.0077	0.032
Example 2	0.006	0.447	0.26	11.30	0.073	0.010	0.21	0.003	0.0052	0.022
Comparative	0.006	0.472	0.37	11.15	0.067	0.009	0.18	0.002	0.0057	0.023
example 1
Comparative	0.008	0.466	0.36	11.17	0.072	0.008	0.22	0.002	0.0079	0.052
example 2

It shows microstructures of a hot-rolled annealed material (2.0t) and a normal cold-rolled annealed material (2.0t) according to reduction rates. Comparative example 1 is a normal 2.0t hot-rolled material that appears to have an average crystal grain size of about 120 μm, which is very coarse. Example 1 shows a microstructure of a material obtained by pre-rolling a hot-rolled steel sheet with a thickness of 3.11 at a reduction rate of about 35% and performing hot annealing, and the crystal grain size appears to be about 60 μm as shown in Table 2, so it may be understood that the crystal grains are refined to a level of 50% as compared to the microstructure of comparative example 1 obtained by annealing the existing hot-rolled 2.0t steel sheet. With this, it may be assumed that crystal grains are refined due to additional generation of dislocations introduced in rolling a hot-rolled material at a reduction rate of 30% or more. Example 2 shows a microstructure of a material obtained by pre-rolling a hot-rolled steel sheet with a thickness of 4.0t at a reduction rate of about 35% and performing hot annealing, and the crystal grain size is refined to a level of about 50 μm, so it may be understood that the higher the pre-rolling reduction rate, the finer the crystal grains. In comparative example 2, a normal cold-rolled annealed material obtained by hot annealing/pickling a 5.0t hot-rolled material and then performing cold rolling at a reduction rate of about 60% appears to have crystal grains of about 55 μm, which is similar to Example 2 in which pre-rolling is performed to a level of about 50%.

TABLE 2
	Thickness of	Thickness after	Pre-rolling	Grain
section	hot rolling	pre-rolling	reduction rate	size
Example 1	3.1 t	2.0 t	35%	59.5	μm
Example 2	4.0 t	2.0 t	50%	50.7	μm
Comparative	2.0 t	2.0 t	0%	121.5	μm
example 1
Comparative	5.0 t	2.0 t	Cold rolling	54.9	μm
example 2			reduction rate
			60%

Table 3 shows formality (R values) of a hot-rolled annealed material and formality of a normal cold annealed material with pre-rolling reduction rates. The R-bar value that represents vertical anisotropy of the material has the same properties in the face direction of the sheet and have different properties in the thickness direction, and as most rolled sheets have planar anisotropy whose plasticity changes even in the face direction, an average of R values measured by stretching in directions of 0, 45 and 90 degrees from the rolling direction (R-bar=(R₀+2R₄₅+R₉₀)/4) is used.

The R-bar value in comparative 1 (with a normal 2.0t hot-rolled annealed material) is about 1.01, which is very poor, but it may be understood that with a gradual increase in pre-rolling reduction rate, the R-bar value gradually increases. Furthermore, the R-bar value in Example 2 (with a hot-rolled annealed material that goes through 50% pre-rolling) is about 1.21, which is similar to the R-bar value in comparative example 2 (with a normal cold-rolled annealed material).

TABLE 3
		Thick-
	Thick-	ness	Pre-
	ness	after	rolling
	of hot	pre-	reduction
section	rolling	rolling	rate	R0	R45	R90	R-bar
Example 1	3.1t	2.0t	35%	0.77	1.02	1.51	1.08
Example 2	4.0t	2.0t	50%	1.16	0.99	1.7	1.21
Comparative	2.0t	2.0t	0%	0.54	0.77	1.01	0.77
example 1
Comparative	5.0t	2.0t	Cold	1.22	0.85	2.14	1.27
example 2			rolling
			reduction
			rate 60%

Table 4 shows tensile properties of each material, and there is no noticeable difference in tensile strength between Example 2 (with a hot-rolled annealed 2.0t material after about 50% of pre-rolling) and comparative example 2 (with a normal cold-rolled annealed material) but the yield strength appears to be higher by about 10% or more in Example 2. With this, it is determined that the pre-rolled material exhibits higher yield strength than the normal cold-rolled annealed material because the pre-rolled material has additional dislocations introduced thereto and goes through only one hot annealing process while the normal cold-rolled material goes through a total of 2 or more annealing processes comprising hot annealing and cold annealing. It is determined that these characteristics may not only be applied to product groups requiring high-strength of the material, but also help extend the lifespan of the existing products.

TABLE 4
			Pre-
	Thickness	Thickness	rolling
	of hot	after pre-	reduction
section	rolling	rolling	rate	YS (MPa)	TS (MPa)	TS/YS	EL(%)
Example 1	3.1t	2.0t	35%	306	415	1.36	33
Example 2	4.0t	2.0t	50%	293	405	1.38	36
Comparative	2.0t	2.0t	0%	270	419	1.55	34
example 1
Comparative	5.0t	2.0t	Cold	261	397	1.52	35
example 2			rolling
			reduction
			rate 60%

INDUSTRIAL APPLICABILITY

According to an embodiment of the disclosure, a hot-rolled ferritic stainless steel sheet exhibits similar formality to a cold-rolled material despite being a hot-rolled material, so the industrial applicability is acknowledged.

Claims

1. A hot-rolled ferritic stainless steel sheet with excellent formability having a value of R-bar being 1.08 or more and satisfying a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5, after hot rolling a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.1% of N, 0.1% or less of Al and the remainder having Fe and unavoidable impurities and pre-rolling the steel at a reduction rate of 30% or more.

2. The hot-rolled ferritic stainless steel sheet with excellent formability of claim 1, wherein a ferrite crystal grain size is 60 μm or less when the crystal grain size is measured in an electron backscattering diffraction analysis (EBSD) method with intergranular misorientation ranging from 15° to 180°.

3. A method of manufacturing a hot-rolled ferritic stainless steel sheet with excellent formability, the method comprising:

manufacturing a slab by continuously casting a steel comprising, in percent by weight (wt %), 0.001 to 0.1% of C, 10.0 to 14.0% of Cr, 0.001 to 0.5% of Ti, 0.001 to 0.5% of Nb, 0.001 to 1.5% of Ni, 0.001 to 1.5% of Mn, 0.001 to 1.0% of Cu, 0.001 to 2.0% of Si, 0.001 to 0.1% of N, 0.1% or less of Al and the remainder having Fe and unavoidable impurities;

reheating the manufactured slab;

hot rolling the reheated slab;

performing pre-rolling at a reduction rate of 30% or more to satisfy a value of R-bar being 1.08 or more and a ratio of yield strength (YS) and tensile strength (TS), TS/YS≤1.5; and

performing hot annealing.