Austenitic light-weight high-strength steel with excellent properties of welds, and method of manufacturing the same

Abstract

The present invention relates to an austenitic light-weight high-strength steel with excellent properties of welds, and a method of manufacturing the same, the method including: (a) hot-rolling a steel including 20 wt % to 30 wt % of manganese (Mn), 6 wt % to 12 wt % of aluminum (Al), 0.6 wt % to 1.5 wt % of carbon (C), 0.3 wt % to 0.95 wt % of vanadium (V), and a remaining amount of iron (Fe) and other unavoidable impurities; (b) homogenizing the hot-rolled steel; and (c) aging the homogenized steel.

Claims

1. A method of manufacturing an austenitic steel, the method comprising: hot-rolling a steel including 20 wt % to 30 wt % of manganese (Mn), 6 wt % to 12 wt % of aluminum (Al), 0.6 wt % to 1.5 wt % of carbon (C), 0.3 wt % to 0.95 wt % of vanadium (V), and a remaining amount of iron (Fe) and other unavoidable impurities; homogenizing the hot-rolled steel; and aging the homogenized steel, wherein hot-rolling the steel comprises: hot-rolling the steel under a finish rolling temperature ranging from 900 C. to 1000 C.; and cooling the steel to 600 C. or less, wherein cooling the steel comprises cooling the steel at an average cooling rate ranging from 10 C./sec to 50 C./sec, and wherein aging the homogenized steel comprises: aging the homogenized steel at a temperature ranging from 540 C. to 560 C. for 10 minutes or more; and cooling the steel to a temperature of 200 C. or less, at an average cooling rate of 10 C./sec or less.

2. The method of claim 1, wherein the steel further includes 0.02 wt % to 0.06 wt % of niobium (Nb).

3. The method of claim 2, wherein a total amount of niobium and vanadium is 0.35 wt % to 0.95 wt %.

4. The method of claim 1, wherein homogenizing the hot-rolled steel comprises: homogenizing the hot-rolled steel at a temperature ranging from 1000 C. to 1200 C. for a time ranging from 1 to 3 hours; and cooling the steel to a temperature of 600 C. or less, at an average cooling rate of 10 C./sec or more.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a flow chart schematically illustrating a method of manufacturing an austenitic light-weight high-strength steel according to an exemplary embodiment of the present invention.

(2) FIG. 2 illustrates tensile test results of weld heat-affected zone of developed steels 1 and 2 and existing steel.

(3) FIG. 3 illustrates a fine structure of the weld heat-affected zone of the existing steel.

(4) FIG. 4 illustrates a fine structure of the weld heat-affected zone of the developed steel 1.

DETAILED DESCRIPTION

(5) Hereinafter, an austenitic light-weight high-strength steel with excellent properties of welds according to the present invention, and a method of manufacturing the same, are described in detail with reference to the accompanying drawings.

(6) The austenitic light-weight high-strength steel with excellent properties of welds according to the present invention includes 20 wt % to 30 wt % of manganese (Mn), 6 wt % to 12 wt % of aluminum (Al), 0.6 wt % to 1.5 wt % of carbon (C), and 0.3 wt % to 0.95 wt % of vanadium (V).

(7) In addition, the austenitic light-weight high-strength steel according to the present invention preferably further includes 0.02 wt % to 0.06 wt % of niobium (Nb).

(8) In addition to the above-described components, the austenitic light-weight high-strength steel includes a remaining amount of iron (Fe) and other unavoidable impurities.

(9) Alloy components of the austenitic light-weight high-strength steel according to the present invention is deduced to overcome problems such as limitation in elongation due to formation of ferrite, limitation in elongation due to formation of Mn phase, deterioration of tensile strength due to crystal grain growth in welds, and the like. Hereinafter, role and amount of each component included in the austenitic light-weight high-strength steel according to the present invention are described.

(10) Manganese (Mn)

(11) Manganese (Mn) is an austenite stabilizing element, and needs to have an amount of 20 wt % or more relative to total weight of the steel in order to manufacture an austenitic light-weight high-strength steel having a fine structure close to an austenite single phase.

(12) Meanwhile, when an amount of manganese is more than 30 wt %, which is excessive, the formation of Mn phase reduces elongation. Therefore, in the present invention, the amount of manganese is limited to be 30 wt % or less relative to total weight of the steel.

(13) Aluminum (Al)

(14) Aluminum (Al) is an essential element for weight lightening, and has an amount of 6 wt % or more relative to total weight of the steel in order to increase a light-weight effect.

(15) Meanwhile, aluminum is ferrite stabilizing element, and when an amount of aluminum is more than 12 wt %, which is excessive, the formation of austenite phase may be interfered, and elongation may be reduced by the formation of ferrite, and therefore, in the present invention, the amount of aluminum is limited to be 12 wt % or less relative to total weight of the steel.

(16) Carbon (C)

(17) Carbon (C) is a strong austenite stabilizing element, and is required for manufacturing an austenitic light-weight high-strength steel, and is effective for increasing tensile strength due to an effect of enhancing solidification.

(18) The carbon preferably has an amount of 0.6 wt % to 1.5 wt % relative to total weight of the steel. When the amount of carbon is less than 0.6 wt %, an effect obtained by adding carbon is not sufficient. On the other hand, when the amount of carbon is more than 1.5 wt %, elongation may be reduced due to formation of excessive carbides, and may cause crack at the time of rolling.

(19) Vanadium (V)

(20) Vanadium (V) is a strong carbide forming element and is effective for increasing tensile strength according to enhancement of precipitation.

(21) The vanadium preferably has an amount of 0.3 wt % to 0.95 wt % relative to total weight of the steel. When the amount of vanadium is less than 0.3 wt %, an effect obtained by adding vanadium is not sufficient. On the other hand, when the amount of vanadium is more than 0.95 wt %, formation of coarse precipitates is promoted, such that the effect of enhancing precipitation may be inhibited, and elongation may be largely reduced.

(22) Niobium (Nb)

(23) Niobium (Nb) is a strong carbide forming element together with vanadium (V), and is effective for increasing tensile strength according to enhancement of precipitation. Further, niobium forms precipitates being stable at a high temperature, thereby inhibit the crystal grain growth in the weld heat-affected zone to prevent deterioration of properties of welds.

(24) When the steel includes niobium, the niobium preferably has an amount of 0.02 wt % to 0.06 wt % relative to total weight of the steel. When the amount of niobium is less than 0.02 wt %, an effect obtained by adding niobium is not sufficient. On the other hand, when the amount of niobium is more than 0.06 wt %, formation of precipitates is promoted, such that the effect of enhancing precipitation may be rather reduced.

(25) Meanwhile, when the steel includes niobium having the above preferable amount, a total amount of niobium and vanadium is more preferably 0.35 wt % to 0.95 wt % relative to total weight of the steel. It is because when the total amount of niobium and vanadium satisfies the above-described range, tensile strength may be 900 MPa or more and elongation may be 40% or more. Meanwhile, when the total amount of niobium and vanadium is more than 0.95 wt %, which is excessive, elongation may be reduced.

(26) Sulfur (S), Phosphorus (P)

(27) Sulfur (S) and phosphorus (P) are factors causing segregation in manufacturing steel, which deteriorates toughness and ductility of the steel. In addition, sulfur is bound to manganese (Mn), thereby forming MnS inclusion, which deteriorates ductility.

(28) Therefore, the most preferably, sulfur and phosphorus are not included, and in the case in which sulfur and phosphorus are included as impurities, it is preferable to limit amounts of sulfur (S) and phosphorus (P) to be 0.01 wt % or less and 0.02 wt % or less, respectively.

(29) The austenitic light-weight high-strength steel including the above-described alloy components according to the present invention has a fine structure including austenite and carbides according to a manufacturing process to be described below. Here, the steel includes 90% or more of austenite in an area ratio. Further, the carbides include -carbide produced by the aging process, and precipitates formed by adding vanadium and niobium.

(30) Further, in the austenitic light-weight high-strength steel according to the present invention, tensile strength of a weld heat-affected zone after welding may be 80% or more relative to strength of a basic material, such that excellent properties of welds may be exhibited.

(31) In addition, when the total amount of niobium and vanadium is 0.35 wt % to 0.95 wt % in the austenitic light-weight high-strength steel according to the present invention, tensile strength of 900 MPa or more, yield strength of 650 MPa or more, and high elongation of 40% or more may be exhibited.

(32) Hereinafter, a method of manufacturing an austenitic light-weight high-strength steel with excellent properties of welds according to the present invention is described.

(33) FIG. 1 is a flow chart schematically illustrating a method of manufacturing an austenitic light-weight high-strength steel according to an exemplary embodiment of the present invention.

(34) The method of manufacturing an austenitic light-weight high-strength steel according to the present invention may include hot-rolling (S110), homogenizing (S120), and aging (S130).

(35) First, in the hot-rolling (S110), a steel including 20 wt % to 30 wt % of manganese (Mn), 6 wt % to 12 wt % of aluminum (Al), 0.6 wt % to 1.5 wt % of carbon (C), 0.3 wt % to 0.95 wt % of vanadium (V), and a remaining amount of iron (Fe) and other unavoidable impurities is subjected to hot-rolling and cooling.

(36) Here, as described above, the steel may further include 0.02 wt % to 0.06 wt % of niobium (Nb), and in this case, a total amount of niobium and vanadium is preferably 0.35 wt % to 0.95 wt %.

(37) The steel may be re-heated at about 1150 C. to 1250 C. for 1 to 3 hours before the hot-rolling.

(38) More specifically, the hot-rolling may include hot-rolling the steel under a finish rolling temperature condition of 900 C. or more, more preferably, 900 C. to 1000 C., and cooling the steel up to 600 C. or less, preferably, 600 C. to 400 C., at an average cooling rate of 10 C./sec or more, preferably, 10 to 200 C./sec. When the finish rolling temperature is less than 900 C., abnormal grains may be mixed. In addition, when the average cooling rate is less than 10 C./sec, a large amount of coarse carbides may be formed at the time of cooling. Further, when a cooling end temperature is more than 600 C., a large amount of coarse carbides may be formed. The cooling in the present step is preferably water-cooling.

(39) Next, in the homogenizing (S120), the hot-rolled steel is homogenized.

(40) More specifically, the homogenizing (S120) may include homogenizing the hot-rolled steel at 1000 C. to 1200 for 1 to 3 hours, and cooling the steel up to 600 C. or less, more preferably, room temperature, at an average cooling rate of 10 C./sec or more, preferably, 10 to 200 C./sec. When a temperature for the homogenizing is less than 1000 C., an effect obtained by the homogenizing is not sufficient, and when the temperature for the homogenizing is more than 1200 C., toughness and ductility may be deteriorated due to coarse crystal grains. Further, when the average cooling rate is less than 10 C./sec after the homogenizing, a large amount of coarse carbide may be formed at the time of cooling. Further, when a cooling end temperature is more than 600 C., a large amount of coarse carbides may be formed. The cooling in the present step is preferably water-cooling.

(41) Next, in the aging (S130), the homogenized steel is subjected to aging. By the aging, strength may be improved, and fine -carbide may be formed to improve mechanical properties of the steel.

(42) The aging may include aging the homogenized steel at 55010 C. for 10 minutes or more, and cooling the steel up to 200 C. or less, more preferably, room temperature, at an average cooling rate of 10 C./sec or less. When a temperature of the aging is less than 540 C., an effect obtained by the aging is not sufficient, and when a temperature of the aging is more than 560 C., properties may be deteriorated due to precipitation of crystal grains. Further, when the cooling is performed an average cooling rate of more than 10 C./sec after the aging, properties of the steel may be deteriorated. The cooling in the present step is preferably air-cooling.

Example

(43) Hereinafter, constitution and function of the present invention will be described in more detail through preferable exemplary embodiments of the present invention. Meanwhile, these exemplary embodiments are provided by way of example, and accordingly, it should not be interpreted as limiting the scope of the present invention. Descriptions which are not described in the specification can be sufficiently and technically deduced by a person skilled in the technical field, and accordingly, details thereof will be omitted.

(44) 1. Manufacture of Sample

(45) Each ingot having chemical composition shown in Table 1 was manufactured in a vacuum induction melting furnace. Each ingot was re-heated at 1200 C. for 2 hours, followed by hot-rolling under a finish rolling temperature condition of 920 C., and water-cooling up to 550 at an average cooling rate of 50 C./sec, and then air-cooling up to room temperature, thereby manufacturing a steel sheet having a thickness of 4 mm. Then, the steel sheet was homogenized at 1050 C. for 2 hours, and water-cooled up to room temperature at a cooling rate of 20 C./sec. Then, the steel sheet was subjected to aging at 550 C. for 1000 minutes, and air-cooled up to room temperature. In the developed steels as compared to the existing steel, carbides that are stable at high temperature were formed by adding vanadium and niobium, respectively, to inhibit austenite crystal grain growth, and accordingly, light-weight steels in which properties of a basic material and welds are excellent were manufactured.

(46) TABLE-US-00001 TABLE 1 (Unit: wt %) Classification C Mn Al V Nb Fe Sample 1 0.9 30 9 Remaining (Existing Steel) amount Sample 2 0.9 30 9 0.5 Remaining (Developed Steel 1) amount Sample 3 0.9 30 9 0.5 0.04 Remaining (Developed Steel 2) amount Sample 4 0.9 30 9 1.0 Remaining (Compared Steel) amount

(47) 2. Evaluation of Properties

(48) A tensile test was performed on samples 1 to 4, and results thereof were shown in Table 2.

(49) TABLE-US-00002 TABLE 2 Tensile Elongation Classification Strength (MPa) Yield Strength (MPa) (%) Development 900 650 40 Objective Sample 1 892 654 53 (Existing Steel) Sample 2 921 681 43 (Developed Steel 1) Sample 3 992 667 44 (Developed Steel 2) Sample 4 935 655 29 (Compared Steel)

(50) As confirmed in Table 2, it may be appreciated that as compared to the existing steel, the developed steels had high strength.

(51) In particular, in samples 2 and 3 in which a total amount of niobium and vanadium is 0.35 wt % to 0.95 wt %, both of strength and elongation were excellent, but in sample 4 (compared steel) in which more than 0.95 wt % of vanadium is added, elongation was below the target value.

(52) In addition, in sample 3 in which niobium and vanadium are simultaneously added, tensile strength was improved by 100 MPa as compared to sample 1.

(53) FIG. 2 and Table 3 show tensile test results of each weld heat-affected zone of the developed steels 1 and 2 and the existing steel.

(54) In order to confirm properties of welds of the developed steels as compared to the existing steel, the weld heat-affected zone was implemented by using Gleeble simulator, wherein heat input was implemented to be 300 kJ/cm.

(55) TABLE-US-00003 TABLE 3 Tensile Elongation Classification Strength (MPa) Yield Strength (MPa) (%) Sample 1 754 377 68 (Existing Steel) Sample 2 801 441 49 (Developed Steel 1) Sample 3 806 443 40 (Developed Steel 2)

(56) Referring to FIG. 2 and Table 3, it was confirmed that as compared to the existing steel, the developed steels exhibited excellent tensile properties of the weld heat-affected zone, and the sample 3 in which niobium and vanadium are simultaneously added had the highest tensile strength and yield strength. These results come from the carbides such as NbC, (Nb,V)C, VC, and the like, formed by further adding niobium, vanadium, and the like, to thereby contribute to strength, in addition to -carbide which contribute to strength in the existing light-weight steel.

(57) Meanwhile, the present invention has an object of providing a light-weight steel in which a weld heat-affected zone has strength of 80% or more relative to a basic material. As confirmed in Tables 2 and 3, in the existing steel, the yield strength of the weld heat-affected zone was largely reduced to be 80% or less relative to that of the basic material. Meanwhile, in the developed steels, both of the tensile strength and the yield strength of the weld heat-affected zone were 80% or more relative to those of the basic material, thereby satisfying the target values.

(58) FIG. 3 illustrates a fine structure of the weld heat-affected zone of the existing steel, and FIG. 4 illustrates a fine structure of the weld heat-affected zone of the developed steel 1.

(59) As illustrated in FIGS. 3 and 4, as compared to the existing steel, the developed steel had a fine crystal grain size, which is because VC precipitates which are stable at a high temperature are formed by adding 0.5 wt % of vanadium, and due to the VC precipitates, the crystal grain growth at a high temperature is inhibited. The fine crystal grain may be considered as another factor for improving the strength of the weld heat-affected zone of Table 3 in addition to the effect of enhancing precipitation.

(60) According to the method of manufacturing an austenitic light-weight high-strength steel of the present invention, crystal grain growth of a weld heat-affected zone may be inhibited by adding carbide forming elements such as V, Nb, and the like, to the FeCMnAl alloy (Fe, C, Mn and Al are basic components of a light-weight steel), thereby forming precipitates such as VC, NbC, (Nb,V)C, and the like. Accordingly, the austenitic light-weight steel with excellent properties in which strength is 80% or more relative to the basic material, is capable of being manufactured.

(61) Further, the austenitic light-weight high-strength steel according to the present invention may have 900 MPa or more of tensile strength, 650 MPa or more of yield strength, and 40% of elongation by adding an appropriate amount of each of niobium and vanadium, thereby having high formability and high strength.

(62) Although the exemplary embodiments of the present invention have been described, various changes and modifications can be made by those skilled in the art without the scope of the appended claims of the present invention. Such changes and modifications should also be understood to fall within the scope of the present invention. Therefore, the protection scope of the present invention should be determined by the appended claims to be described below.