HIGH STRENGTH STEEL PLATE AND MANUFACTURING METHOD THEREFOR

A high strength steel plate according to an aspect of the present disclosure includes, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfies relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher, and includes a combined structure of tempered martensite and tempered bainite as a microstructure.

Skip to: Description  ·  Claims  · Patent History  ·  Patent History
Description
TECHNICAL FIELD

The present disclosure relates to a high strength steel plate and a manufacturing method therefor, and more particularly, to a high strength steel plate having excellent tensile strength and impact toughness, particularly suitable for a nuclear reactor containment container, and a manufacturing method therefor.

BACKGROUND ART

Various materials are used for the structures and facilities of a nuclear power plant according to the type, usage, and safety properties thereof. In particular, a nuclear reactor containment vessel utilizes a steel material, and A516-70 steel produced by a normalizing process is mainly used as a thick steel plate material.

However, such A516-70 steel has insufficient tensile strength (about 500 Mpa) to ensure the nuclear power plant's safety, and, thus, a range of use thereof may be extremely limited. That is, since the A516-70 steel has relatively low tensile strength, when used to manufacture a nuclear reactor containment vessel, there may be a risk of damage or explosion due to the failure to withstand the high pressure inside. Accordingly, there may be an urgent need to develop a material suitable for a nuclear reactor containment container while having tensile strength of a certain level or more.

In order to improve the tensile strength, if a relatively large amount of expensive alloying elements is added to a steel material or a separate heat treatment is performed, tensile strength may be hardly improved, but an increase in costs due to the addition of the alloying elements may be inevitable, and there may be other incidental problems involved.

Patent Document 1 discloses a high strength steel plate with improved tensile strength, which may be a high strength steel plate that may be used for a nuclear reactor containment vessel. However, the steel plate disclosed in Patent Document 1 has a level of tensile strength that may be used as a steel plate for a nuclear reactor containment vessel, but may not be suitable as a material for a nuclear reactor containment vessel due to deteriorations in low-temperature toughness and nil-ductility transition temperature properties.

(Patent Document 1) Korea Patent Publication No. 10-2010-0076745 (published on Jul. 6, 2010)

DISCLOSURE Technical Problem

According to an aspect of the present disclosure, a high strength steel plate having excellent tensile strength, low-temperature toughness, and nil-ductility transition temperature properties, particularly suitable for a nuclear reactor containment container of a nuclear power plant, and a manufacturing method therefor, may be provided.

The problems of the present disclosure to be solved are not limited to the above-mentioned contents. Those skilled in the art will have no difficulty in understanding additional problems of the present disclosure from the overall contents of this specification.

Technical Solution

According to an aspect of the present disclosure, a high strength steel plate includes, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfies relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher, and includes a combined structure of tempered martensite and tempered bainite as a microstructure.

The tempered martensite may be included in 30 to 60 area % in the microstructure, the tempered bainite may be included in 40 to 70 area % in the microstructure, and the sum of the tempered martensite and the tempered bainite may be 100 area %.

The tempered martensite may be included in 40 to 60 area % in the microstructure, and the tempered bainite may be included in 40 to 60 area % in the microstructure.

A nil-ductility transition temperature of the steel plate may be −50° C. or lower.

Tensile strength of the steel plate may be 600 MPa or more.

Charpy impact toughness of the steel plate may be 250 J or more at −60° C.

A grain aspect ratio (a long axis/short axis ratio) of the microstructure may be 1.1 to 2.5.

According to an aspect of the present disclosure, a method of manufacturing a high strength steel plate, includes: reheating a steel slab at 1050 to 1250° C., the steel slab comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher, rolling the slab in a temperature range of Tnr to Tnr+100° C. to provide a steel plate, austenizing the steel plate in a temperature range of 870 to 950° C., quenching the austenized steel plate to a temperature range of 300° C. or lower, and tempering the quenched steel plate in a temperature range of 595 to 700° C.

A accumulated reduction amount of the rolling may be 50 to 90%.

A grain aspect ratio (a long axis/short axis ratio) of a microstructure of the steel plate by the rolling may be controlled to have a range of 1.1 to 2.5.

The austenizing may be performed for a time period of 1.6*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes).

The tempering may be performed for a time period of 2.4*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes).

Advantageous Effects

According to a preferred aspect of the present disclosure, a high strength steel plate securing a tensile strength of 600 MPa or more, a Charpy impact toughness of 250 J or more at −60° C., and a nil-ductility transition temperature of −50° C. or lower, to be particularly suitable for a nuclear reactor containment container of a nuclear power plant, and a manufacturing method therefor, may be provided.

BEST MODE FOR INVENTION

The present disclosure relates to a high strength steel plate and a manufacturing method therefor, and, hereinafter, preferred embodiments of the present disclosure will be described. Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to embodiments to be described below. These embodiments may be provided to those skilled in the art to further detail the present disclosure.

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

A high strength steel plate according to an embodiment of the present disclosure may include, by weight: 0.05 to 0.2% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities.

Carbon (C): 0.05 to 0.2%

Since carbon (C) may be an effective element for securing strength, the present disclosure may limit a lower limit of the carbon (C) content to 0.05% to prevent a decrease in strength on a matrix phase. When carbon (C) is excessively added, toughness and weldability may be deteriorated, making it unsuitable for use for a nuclear reactor containment container, and the present disclosure may limit an upper limit of the carbon (C) content to 0.2%. Therefore, the carbon (C) content of the present disclosure may be 0.05 to 0.2%, and a more preferable carbon (C) content may be 0.08 to 0.15%.

Silicon (Si): 0.15 to 0.55%

Silicon (Si) may be an element added for a deoxidation effect, a solid solution strengthening effect, and an impact transition temperature increasing effect. Therefore, the present disclosure may limit a lower limit of the silicon (Si) content to 0.15% to achieve this effect. A preferred lower limit of the silicon (Si) content may be 0.2%, and a more preferred lower limit of the silicon (Si) content may be 0.3%. When the silicon (Si) is excessively added, weldability of the steel plate may be deteriorated and an oxide film may be severely formed on a surface of the steel plate. Therefore, the present disclosure may limit an upper limit of the silicon (Si) content to 0.55%. A preferred upper limit of the silicon (Si) content may be 0.5%, and a more preferred upper limit of the silicon (Si) content may be 0.4%.

Manganese (Mn): 0.9 to 1.75%

Manganese (Mn) maybe an effective element for securing strength, and the present disclosure may limit a lower limit of the manganese (Mn) content to 0.9% to achieve this effect. A preferred lower limit of the manganese (Mn) content may be 1.0%, and a more preferred lower limit of the manganese (Mn) content maybe 1.2%. Manganese (Mn) maybe combined with sulfur (S) to forma non-metallic inclusion such as MnS. When manganese (Mn) is added excessively, elongation at room temperature and low-temperature toughness may be deteriorated. Therefore, the present disclosure may limit an upper limit of the manganese (Mn) content to 1.75%. A preferred upper limit of the manganese (Mn) content may be 1.7%, and a more preferred upper limit of the manganese (Mn) content may be 1.6%.

Aluminum (Al): 0.001 to 0.05%

Since aluminum (Al) may be an element as a strong deoxidizer, the present disclosure may limit a lower limit of the aluminum (Al) content to 0.001% for a deoxidation effect in a steelmaking process. When aluminum (Al) is added excessively, the deoxidation effect may be saturated, but manufacturing costs may be increased. The present disclosure may limit an upper limit of the aluminum (Al) content to 0.05%. The aluminum (Al) content is more preferably 0.01 to 0.04%.

Phosphorus (P): 0.03% or less

Phosphorus (P) may be an element that impairs low-temperature toughness. Therefore, P may be desirable to have its content managed to be as low as possible. Since Phosphorus (P) may be an element that may be inevitably contained in a steelmaking process, may take excessive cost to completely remove it, the present disclosure may limit an upper limit of the phosphorus (P) content to 0.03%. A preferred upper limit of the phosphorus (P) content may be 0.02%, and a more preferred upper limit of the phosphorus (P) content may be 0.01%.

Sulfur (S): 0.03% or less

Sulfur (S) maybe also an element that adversely affects low-temperature toughness, together with phosphorus (P). Therefore, S may be desirable to have its content managed to be as low as possible. Since sulfur (S) may be an element that may be inevitably contained in a steelmaking process, like phosphorus (P), and may take excessive cost to completely remove it, the present disclosure may limit an upper limit of the sulfur (S) content to 0.03%. A preferred upper limit of the sulfur (S) content may be 0.02%, and a more preferred upper limit of the sulfur (S) content may be 0.01%.

Chromium (Cr): 0.05 to 0.3%

Since chromium (Cr) may be an element contributing to an increase in strength, the present disclosure may limit a lower limit of the chromium (Cr) content to 0.05% to achieve this effect. Chromium (Cr) may be an expensive element. When Cr is added excessively, it is not preferable from a viewpoint of economic efficiency. Therefore, the present disclosure may limit an upper limit of the chromium (Cr) content to 0.3%. Therefore, the chromium (Cr) content of the present disclosure may be 0.05 to 0.3%, and is more preferably 0.05 to 0.2%.

Nickel (Ni): 0.05 to 0.6%

Nickel (Ni) may be an effective element for improving low-temperature toughness. Therefore, the present disclosure may limit a lower limit of the nickel (Ni) content to 0.05% to achieve this effect. Nickel (Ni) may be an expensive element. When Ni is excessively added, an increase in production cost may occur. Therefore, the present disclosure may limit an upper limit of the nickel (Ni) content to 0.6%. Therefore, the nickel (Ni) content of the present disclosure may be 0.05 to 0.6%, and is more preferably 0.2 to 0.6%.

Copper (Cu): 0.005 to 0.35%

Copper (Cu) may be an effective element for increasing strength. Therefore, the present disclosure may limit a lower limit of the copper (Cu) content to 0.005% to achieve this effect. Copper (Cu) maybe an expensive element. When Cu is excessively added, an increase in production cost may occur. Therefore, the present disclosure may limit an upper limit of the copper (Cu) content to 0.35%. Therefore, the copper (Cu) content of the present disclosure maybe 0.005 to 0.35%, and is more preferably 0.01 to 0.3%.

Molybdenum (Mo): 0.05 to 0.2%

Molybdenum (Mo) may be an alloy element effective for improving strength, and may be an element that prevents crack generation caused by sulfide. Therefore, the present disclosure may limit a lower limit of the molybdenum (Mo) content to 0.05% to achieve this effect. Molybdenum (Mo) maybe also an expensive element. When Mo is excessively added, an increase in production cost may occur. Therefore, the present disclosure may limit an upper limit of the molybdenum (Mo) content to 0.2%. Therefore, the molybdenum (Mo) content of the present disclosure may be 0.05 to 0.2%, and is more preferably 0.1 to 0.2%.

Vanadium (V): 0.005 to 0.07%

Vanadium (V) may be an effective element for improving low-temperature toughness. Therefore, the present disclosure may limit a lower limit of the vanadium (V) content to 0.005% to achieve this effect. Vanadium (V) may be also an expensive element. When V is excessively added, an increase in production cost may occur. Therefore, the present disclosure may limit an upper limit of the vanadium (V) content to 0.07%. Therefore, the vanadium (V) content of the present disclosure maybe 0.005 to 0.07%, and is more preferably 0.01 to 0.07%.

Niobium (Nb): 0.005 to 0.04%

Niobium (Nb) may be an element that may be dissolved in austenite to increase hardenability of the austenite. In addition, niobium (Nb) may be an element that is precipitated as carbonitride (Nb(C,N)) matching with a matrix, together with titanium (Ti) , and may be a major element for obtaining a tensile strength of 600 MPa or more for which the present disclosure seeks. Therefore, the present disclosure may limit a lower limit of the niobium (Nb) content to 0.005% to achieve this effect. When niobium (Nb) is excessively added, coarse precipitates may occur in the process of continuous casting, and Nb may act as a starting point for hydrogen-induced cracking (HIC). Therefore, the present disclosure may limit an upper limit of the niobium (Nb) content to 0.04%. Therefore, the niobium (Nb) content of the present disclosure may be 0.005 to 0.04%, and is more preferably 0.01 to 0.03%.

Calcium (Ca): 0.0005 to 0.005%

Calcium (Ca) may be combined with sulfur (S) to form a CaS precipitate, and may thus be an effective element for suppressing formation of MnS. Therefore, the present disclosure may limit a lower limit of the calcium (Ca) content to 0.0005% to achieve this effect. When calcium (Ca) is excessively added, Ca may react with oxygen in steel to produce CaO, which may be a non-metallic inclusion. Therefore, the present disclosure may limit an upper limit of the calcium (Ca) content to 0.005%. Therefore, the calcium (Ca) content of the present disclosure maybe 0.0005 to 0.005%, and is more preferably 0.001 to 0.003%.

Titanium (Ti): 0.005 to 0.025%

An appropriate content of titanium (Ti) maybe fluidly limited according to the content of nitrogen (N). When the content of titanium (Ti) is relatively small, compared to the content of nitrogen (N), an amount of TiN produced may be relatively small, which may be disadvantageous for fine-graining. When titanium (Ti) is added in an excessive amount, TiN may become coarse during a heating operation to reduce an effect of inhibiting grain growth. Therefore, in consideration of the content (e.g., 0.002 to 0.006%) of nitrogen (N), the content of titanium (Ti) of the present disclosure may be 0.005 to 0.025%, and is more preferably 0.01 to 0.02%.

Nitrogen (N): 0.002 to 0.006%

Nitrogen (N) may be widely known as an element that plays a role in increasing toughness of a base material and impact toughness of a heat-affected zone (HAZ) by forming a TiN precipitate with titanium (Ti) to refine grains. In this regard, according to the present disclosure, nitrogen (N) may be an element that should be added to achieve the purpose of grain refinement. Therefore, the present disclosure may limit a lower limit of the nitrogen (N) content to 0.002% to achieve this effect. When the nitrogen (N) content is excessively added, an amount of TiN may be excessively increased and low-temperature toughness maybe reduced. Therefore, the present disclosure may limit an upper limit of the nitrogen (N) content to 0.006%. Therefore, the nitrogen (N) content of the present disclosure may be 0.002 to 0.006%, and is more preferably 0.002 to 0.004%.

Boron (B): less than 0.0005%

In the present disclosure, the content of boron (B) may be actively suppressed, but excessive cost may be consumed to completely remove boron (B), which may be inevitably introduced during a steelmaking process. Therefore, the present disclosure may limit the boron (B) content to less than 0.0005%. A preferred boron (B) content is 0.0002% or less, and a more preferred boron (B) content is 0.0001% or less.

A high strength steel plate according to an aspect of the present disclosure may satisfy relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher.

Hereinafter, the relationships of the present disclosure will be described in more detail.

Cu+Ni+Cr+Mo: 1.5% or less

Cr+Mo: 0.4% or less

V+Nb: 0.1% or less

Ca/S: 1.0 or higher

The relationships of Cu+Ni+Cr+Mo, Cr+Mo, and V+Nb may be values that are respectively limited in the basic specification (ASTM A20) regarding steel for a pressure vessel, and the content of Cu+Ni+Cr+Mo may be limited to 1.5% or less, the content of Cr+Mo may be limited to 0.4% or less, and the content of V+Nb may be limited to 0.1% or less. In addition, a ratio of Ca/s maybe an essential composition ratio of spheroidizing an MnS inclusion to improve hydrogen-induced crack resistance. When the ratio of Ca/s is less than 1.0, it maybe difficult to expect the effect, the ratio may be limited to satisfy 1.0 or more.

Hereinafter, the microstructure of the present disclosure will be described in more detail.

A high strength steel plate according to an aspect of the present disclosure may include a combined structure of tempered martensite and tempered bainite as a microstructure.

Microstructure: combined structure of tempered martensite and tempered bainite

When quenching and tempering a steel material provided with the above-described alloy composition, a microstructure of the steel material may have a microstructure of tempered martensite and tempered bainite. In the present disclosure, the tempered martensite and the tempered bainite may include 30 to 60 area % and 40 to 70 area %, respectively, and a tensile strength of 600 MPa, a nil-ductility transition temperature of −50° C. or lower, and a Charpy impact toughness of 250 J or more at −60° C. may be effectively secured. A preferred area fraction of tempered martensite is 40 to 60%, and a preferred area fraction of tempered bainite is 40 to 60%. In addition, the sum of area fractions of the tempered martensite and the tempered baitite may be 100%.

Grain Aspect Ratio: 1.1≤Long axis/Short axis≤2.5

In the present disclosure, in order to secure high impact toughness and strength, a grain aspect ratio (a ratio of long axis/short axis) may be controlled within a certain range, and the grain aspect ratio may be controlled by a rolling (a recrystallization control rolling) process. When the grain aspect ratio is less than 1.1, a shape of the grain maybe rounded, surface energy thereof may become small, and it maybe difficult to expect refinement of the grain. Therefore, it may be difficult to secure sufficient impact toughness and strength. In addition, when the grain aspect ratio exceeds 2.5, a rolling load for forming the grain becomes too high, and impact toughness may be lowered, which is not preferable. Therefore, the present disclosure may limit the grain aspect ratio (the ratio of long axis/short axis) to have a range of 1.1 to 2.5.

Hereinafter, a manufacturing method of the present disclosure will be described in more detail.

A high strength steel plate according to an aspect of the present disclosure may be manufactured by reheating a steel slab at 1050 to 1250° C., the steel slab including, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher, rolling the slab in a temperature range of Tnr to Tnr+100° C. to provide a steel plate, austenizing the steel plate in a temperature range of 870 to 950° C., quenching the austenized steel plate to a temperature range of 300° C. or lower, and tempering the quenched steel plate in a temperature range of 595 to 700° C.

Since a alloy composition and a content of the slab of the present disclosure correspond to the alloy composition and the content of the high strength steel plate described above, a description of the alloy composition and the content of the slab of the present disclosure may be replaced with the description of the alloy composition and the content of the steel plate described above.

Slab Reheating Operation: 1050 to 1250° C.

In the present disclosure, a slab provided with the above-described alloy composition may be reheated at a temperature range of 1050 to 1250° C. This is because, when a reheating temperature thereof is less than 1050° C., it may be difficult to sufficiently dissolve solute atoms, and when a reheating temperature thereof exceeds 1250° C., an austenite grain size may be excessively coarsened and properties of a steel plate may be deteriorated.

Recrystallization Control Rolling Operation: a temperature range of Tnr to (Tnr+100° C.), an accumulated reduction amount of 50 to 90% at a rolling reduction ratio of 10% or more per rolling pass

The recrystallization control rolling operation refers to a rolling operation to be performed at a temperature, equal to or higher than an unrecrystallized temperature. In this case, the unrecrystallized temperature Tnr may be derived by the following Equation 1, which has been already known. In the following Equation 1, a unit of each alloy element is weight%.


Tnr(° C)=887-464×C+890×Ti+363×Al-357×Si+(6445×Nb-644×Nb1/2)+(732×V-230×V1/2)   [Equation 1]

In order to improve strength, it may be necessary to refine an average particle diameter of prior austenite to 30 pm or less in the recrystallization control rolling operation. When the average particle diameter of the prior austenite exceeds 30 μm, strength and toughness of a product may not be sufficiently exhibited. Therefore, a safety level high enough for a nuclear reactor containment vessel may not be guaranteed. To this end, in the present disclosure, the rolling operation may be performed in a temperature range of Tnr to Tnr+100° C.

In this case, a rolling reduction ratio of 10% or more maybe applied per rolling pass, to finally perform the rolling operation in an accumulated reduction amount of 50 to 90%. Such a reduction amount may be provided to control an average size (30 μm or less) of a microstructure required in the present disclosure and a grain aspect ratio (a long axis/short axis ratio) to 1.1 to 2.5. Therefore, when the accumulated reduction amount is less than 50%, it may be difficult to expect a refinement effect of the microstructure and a control effect of the grain aspect ratio. When the accumulated reduction amount exceeds 90%, a rolling load may be excessively applied, which may cause a problem in process.

Heat Treatment and Quenching Operation: quenching after austenizing the steel plate for a time period of 1.6*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes) in a temperature range of 870 to 950° C.

The quenching operation may be an important process for obtaining a combined structure of tempered martensite and tempered bainite, and may be necessary to strictly control process conditions to form a microstructure capable of securing a tensile strength of 600 MPa or more, a −60° C. Charpy impact toughness of 250 J or more, and a nil-ductility transition temperature property of −50° C. or lower.

In the present disclosure, the austenizing operation may be performed for a time period of 1.6*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes) in a temperature range of 870 to 950° C. The austenizing operation may be a heat treatment for austenizing the structure before the quenching operation. When a temperature range of the heat treatment is less than 870° C., it may be difficult to re-solidify the solute elements, and thus it may be difficult to secure strength. When a temperature range of the heat treatment exceeds 950° C., growth of grains may occur and coarse grains may occur, to impair low-temperature toughness. Therefore, a temperature range of the austenizing operation of the present disclosure may be limited to a temperature range of 870 to 950° C.

In addition, in the present disclosure, the austenizing operation maybe performed for a time period of 1.6*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes). When a time period of the austenizing operation is excessively short, an effect of sufficient austenizing may not be expected due to insufficient heating time, and it may be difficult to homogenize the structure. When a time period of the austenizing operation is excessively long, production time may be prolonged and productivity may be deteriorated. Therefore, a time period of the austenizing operation of the present disclosure may be limited to 1.6*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes). For reference, in the steel plate manufacturing process, when 1.6*t is set as a heating time period, and a target temperature is reached, 10 to 30 minutes may be set as a maintenance time period to perform the austenizing operation.

The steel plate, after the austenizing operation, may be quenched, preferably water-cooled, to be transformed to a combined structure of martensite and bainite. Conditions for the quenching operation in the present disclosure is not particularly limited, and any rapid quenching method including a water cooling operation may be applied to the quenching operation of the present disclosure. In order to obtain a microstructure desired by the present disclosure, after the austenizing operation is finished, the steel plate maybe cooled to a temperature range of 300° C. or lower.

Tempering Operation: 2.4×t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes) in a temperature range of 595 to 700° C.

In the present disclosure, in order to secure excellent tensile strength, nil-ductility transition temperature, and low-temperature toughness properties, a tempering operation of the quenched steel material to 300° C. or lower may be used to remove residual stress in a structure thereof. Therefore, tempered martensite and tempered bainite may be formed.

A temperature range of the tempering operation of the present disclosure may be limited to 595 to 700° C. This may be because, when a temperature range of the tempering operation is less than 595° C., carbides and the like may be not smoothly precipitated, and when a temperature range of the tempering operation exceeds 700° C., strength of the steel material may be lowered.

In addition, the tempering operation of the present disclosure maybe carried out for a time period of 2.4*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes) to obtain a sufficient tempering effect. For reference, in the steel plate manufacturing process, when 2.4*t is set as a heating time period, and a target temperature is reached, 10 to 30 minutes may be set as a maintenance time period to perform the tempering operation.

MODE FOR INVENTION

Hereinafter, the present disclosure will be described in more detail through examples. However, it may be necessary to note that the embodiments described below may be only intended to further illustrate the present disclosure and may be not intended to limit the scope of the present disclosure.

A slab provided with the alloy composition of Table 1 below was prepared.

TABLE 1 Composition (wt %) IS a IS b IS c CS d CS e CS f C 0.10 0.09 0.12 0.06 0.07 0.09 Mn 1.51 1.58 0.92 1.30 1.35 0.78 Al 0.02 0.03 0.032 0.035 0.030 0.032 Si 0.35 0.36 0.36 0.35 0.34 0.36 P 0.009 0.010 0.008 0.008 0.010 0.010 S 0.0010 0.0008 0.0011 0.0013 0.0014 0.0012 Cu 0.03 0.04 0.03 0.05 — — Ni 0.50 0.55 0.53 0.05 0.15 0.10 Cr 0.05 0.05 0.06 0.03 0.05 0.04 Mo 0.15 0.18 0.17 0.15 0.10 0.16 V 0.030 0.025 0.030 0.003 0.005 0.030 Nb 0.012 0.014 0.013 0.013 0.012 0.015 B — — — 0.0015 0.0012 0.0007 Ti 0.012 0.010 0.013 0.013 0.012 0.013 N 0.0028 0.0035 0.0034 0.0028 0.0035 0.0032 Ca 0.0020 0.0019 0.0021 0.0018 0.0021 0.0020 IS: Inventive Steel CS: Comparative Steel

Test pieces were prepared by performing a reheating operation, a recrystallization control rolling operation, an austenizing operation, a quenching operation, and a tempering operation using respective slabs made of the compositions of Inventive Steel and Comparative Steel, as illustrated in Table 2 below. Properties such as strength, low-temperature toughness, and nil-ductility transition temperature were evaluated, and the results therefrom are illustrated in Table 3 below. In Table 3 below, the low-temperature impact toughness may be evaluated as a Charpy impact energy value obtained by performing a Charpy impact test on a specimen having a V notch at −60° C. In addition, the nil-ductility transition temperature may be a result value according to the drop-weight test transition temperature set by the ASTM E208-06 method.

TABLE 2 Recrystallization Steel Slab Control Rolling Plate Reheating Rolling Cumulative Grain Austenizing Tempering Thickness Temp. Temp. Reduction Amount Aspect Temp. Temp. Condition (mm) (° C.) (° C.) (%) Ratio* (° C.) (° C.) IS a a-1 45 1200 780 60 1.75 900 680 a-2 80 1180 780 55 1.95 920 660 a-3 100 1100 790 50 1.25 910 650 a-4 50 1100 790 45 1.01 910 660 IS b b-1 45 1150 780 70 2.15 910 680 b-2 80 1100 780 60 2.00 920 660 b-3 100 1100 790 55 1.65 900 650 IS c C 50 1150 780 75 1.98 900 660 CS d d-1 45 1200 780 20 1.02  920** 680 d-2 100 1150 790 30 1.05  900** 650 CS e E 100 1100 780 40 1.06  900** 650 CS f f 80 1150 790 55 1.03 900 650 IS: Inventive Steel CS: Comparative Steel *Grain aspect ratio: Long grain/short grain **Quenching temperatures of Comparative Steel are normalizing temperatures

TABLE 3 Tempered Tempered Martensite Bainite −60° C. NDT Structural Structural Impact Transition Fraction Fraction YS TS Toughness Temp. Condition (%) (%) (MPa) (MPa) (J)*** (° C.)**** IS a a-1 56 44 634 649 334 −80 IE 1 a-2 51 49 641 641 324 −70 IE 2 a-3 48 52 628 634 313 −65 IE 3 a-4 62 38 580 701 58 −40 CE 1 IS b b-1 58 42 642 660 324 −85 IE 4 b-2 50 50 648 652 318 −70 IE 5 b-3 45 55 634 635 334 −70 IE 6 IS c C 55 45 542 650 320 −80 IE 7 CS d d-1 85 15 370 639 180 −40 CE 2 d-2 80 20 365 630 172 −45 CE 3 CS e E 82 18 358 630 193 −40 CE 4 CS f F 85 15 443 650 140 −30 CE 5 IE: Inventive Example CE: Comparative Example IS: Inventive Steel CS: Comparative Steel ***Impact toughness: impact toughness in a T direction (having a V-notch in a direction, perpendicular to a rolling direction) ****NDT transition temperature: transition temperature of the drop-weight test conducted by the ASTM208-06 method.

As in the results of Tables 2 and 3, it can be seen that Inventive Examples 1 to 7 have microstructures of 30 to 60% of tempered martensite and 40 to 70% of tempered bainite, and secure a tensile strength of 600 MPa or more, an impact toughness of 300 J or more at −60° C., and a nil-ductility transition temperature property of −50° C. or lower.

In a case of Comparative Example 1, it can be seen that, since a steel composition satisfies the defined steel composition of the present disclosure, but an accumulated reduction amount of a recrystallization control rolling operation does not satisfy the defined scope of the present disclosure, the area fractions of a microstructure defined by the present disclosure are not satisfied, and a nil-ductility transition temperature property at −50° C. or lower is, thus, not secured.

In addition, in cases of Comparative Examples 2 to 5, it can be seen that, since steel compositions do not satisfy the defined steel composition of the present disclosure, a microstructure has 80 area % or more of tempered martensite and 20 area % or less of tempered bainite, and tensile strength, impact toughness, and nil-ductility transition temperature properties are thus deteriorated.

Therefore, since a steel plate according to an embodiment of the present disclosure may control a steel composition, a microstructure, and manufacturing operations under optimal conditions, to secure tensile strength of 600 MPa or more, Charpy impact toughness of 250 J or more at −60° C., and a nil-ductility transition temperature of −50° C. or lower, a high strength steel plate having properties suitable for a nuclear reactor containment vessel may be provided.

While example embodiments have been illustrated and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present disclosure as defined by the appended claims.

Claims

1. A high strength steel plate comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher, and comprising a combined structure of tempered martensite and tempered bainite as a microstructure.

2. The high strength steel plate according to claim 1, wherein the tempered martensite comprises 30 to 60 area % in the microstructure, the tempered bainite comprises 40 to 70 area % in the microstructure, and the sum of the tempered martensite and the tempered bainite is 100 area %.

3. The high strength steel plate according to claim 2, wherein the tempered martensite comprises 40 to 60 area % in the microstructure, and the tempered bainite comprises 40 to 60 area % in the microstructure.

4. The high strength steel plate according to claim 1, wherein a nil-ductility transition temperature of the steel plate is −50° C. or lower.

5. The high strength steel plate according to claim 1, wherein tensile strength of the steel plate is 600 MPa or more.

6. The high strength steel plate according to claim 1, wherein Charpy impact toughness of the steel plate is 300J or more at −60° C.

7. The high strength steel plate according to claim 1, wherein a grain aspect ratio (a long axis/short axis ratio) of the microstructure is 1.1 to 2.5.

8. A method of manufacturing a high strength steel plate, comprising:

reheating a steel slab at 1050 to 1250° C., the steel slab comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu+Ni+Cr+Mo: 1.5% or less, Cr+Mo: 0.4% or less, V+Nb: 0.1% or less, and Ca/S: 1.0 or higher,
rolling the slab in a temperature range of Tnr to Tnr+100° C. to provide a steel plate,
austenizing the steel plate in a temperature range of 870 to 950° C.,
quenching the austenized steel plate to a temperature range of 300° C. or lower, and
tempering the quenched steel plate in a temperature range of 595 to 700° C.

9. The method according to claim 8, wherein an accumulated reduction amount of the rolling is 50 to 90%.

10. The method according to claim 8, wherein a grain aspect ratio (a long axis/short axis ratio) of a microstructure of the steel plate by the rolling is controlled to have a range of 1.1 to 2.5.

11. The method according to claim 8, wherein the austenizing is performed for a time period of 1.6*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes).

12. The method according to claim 8, wherein the tempering is performed for a time period of 2.4*t (where, t denotes a thickness (mm) of the steel plate)+(10 to 30 minutes).

Patent History
Publication number: 20200347478
Type: Application
Filed: Nov 28, 2018
Publication Date: Nov 5, 2020
Inventor: Soon-Taik Hong (Pohang-si, Gyeongsangbuk-do)
Application Number: 16/957,021
Classifications
International Classification: C21D 9/46 (20060101); C22C 38/58 (20060101); C22C 38/50 (20060101); C22C 38/48 (20060101); C22C 38/46 (20060101); C22C 38/44 (20060101); C22C 38/42 (20060101); C22C 38/06 (20060101); C22C 38/02 (20060101); C22C 38/00 (20060101); C21D 8/02 (20060101); C21D 6/00 (20060101);