CN112930415A - Austenitic high manganese steel material for ultra-low temperature use excellent in shape and method for producing same - Google Patents
Austenitic high manganese steel material for ultra-low temperature use excellent in shape and method for producing same Download PDFInfo
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D2211/001—Austenite
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Abstract
According to one aspect of the present invention, an austenitic high manganese steel for ultra-low temperature use having excellent shape, comprises, in weight%: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: 1% or less (excluding 0%), P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance Fe and other unavoidable impurities, wherein the austenite is contained by 95% by area or more as a microstructure, the Charpy impact toughness at-196 ℃ is 30J or more (based on 5mm thickness), and the difference between the maximum heights of peaks and valleys formed in a region of 2m or less in the rolling direction may be 10mm or less.
Description
Technical Field
The present invention relates to an austenitic high-manganese steel material and a method for producing the same, and more particularly to an austenitic high-manganese steel material for ultra-low temperature use which is excellent in ultra-low temperature toughness and shape, and a method for producing the same.
Background
In the austenitic high manganese steel, the contents of manganese (Mn) and carbon (C) which are elements for improving the stability of austenite are adjusted, so that the austenite is stable even in a normal temperature or ultra-low temperature environment, and further has high toughness, and therefore, the austenitic high manganese steel has particularly suitable physical properties as a material for ultra-low temperature structures such as LNG storage tanks and LNG transfer tanks.
However, high manganese (Mn) steel has high deformation resistance at high temperatures, and particularly in the case of thin plate materials, it is difficult to ensure a uniform shape in the longitudinal direction depending on rolling passes, reduction, and the like. If the shape of the hot rolled material is poor, the safety of cooling is lowered, and equipment damage and the like may be caused in a process such as conveyance. Further, if the hot rolled material is poor in shape in the longitudinal direction, subsequent operations such as shape straightening operations are required, which is not preferable in terms of economy and productivity. Further, there is a technical limitation in ensuring a uniform shape even if a shape correction operation is further performed after cooling. Therefore, there is a need for a high manganese steel material and a method for manufacturing the same, which can provide the steel material with excellent shape uniformity without additional operations such as shape fixation.
Prior art documents
Patent document 1: korean patent laid-open publication No. 10-1994-0002370 (1994.02.17 publication)
Disclosure of Invention
Technical problem
According to one aspect of the present invention, an austenitic high-manganese steel material for ultra-low temperatures having an excellent shape and a method for producing the same can be provided.
The problem to be solved by the present invention is not limited to the above. Other problems of the present invention will be understood by those skilled in the art without any difficulty from the overall contents of the present specification.
Technical scheme
According to one aspect of the present invention, an austenitic high manganese steel for ultra-low temperature use having excellent shape, comprises, in weight%: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: greater than 0% and 1% or less, P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance Fe and other unavoidable impurities, wherein the austenite is contained by 95% by area or more as a microstructure, the Charpy impact toughness at-196 ℃ is 30J or more (based on 5mm thickness), and the difference between the maximum heights of peaks and valleys formed in a region of 2m or less in the rolling direction may be 10mm or less.
The grain size of the austenite can be 5-150 μm.
The steel material may have a yield strength of 350MPa or more, a tensile strength of 700MPa or more, and an elongation of 40% or more.
The austenitic high-manganese steel material for ultra-low temperature use excellent in shape according to one aspect of the present invention can be produced by: heating a steel billet once at a temperature ranging from 1050 to 1300 ℃, wherein the steel billet comprises the following components in percentage by weight: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: greater than 0% and 1% or less, P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance of Fe and other unavoidable impurities; performing primary hot rolling of the heated slab at a finish rolling temperature of 800 to 1100 ℃ at a total reduction rate of 35 to 80% to provide an intermediate material; carrying out secondary heating on the intermediate material at the temperature of 1050-1300 ℃; secondarily hot rolling the secondarily heated intermediate material at a finish rolling temperature of (Tnr-120) to Tnr ℃ to provide a hot rolled material; and cooling the hot-rolled material to a temperature range of 600 ℃ or lower at a cooling rate of 1 to 100 ℃/s, and controlling the total reduction ratio of the intermediate material in the temperature range of (Tnr-120) to Tnr ℃ in the secondary hot rolling to 5 to 25%.
In the hot-rolled material after finishing cooling, a difference between maximum heights of peaks and valleys formed in a region within 2m in a rolling direction may be within 10 mm.
The above-described solutions to the technical problems do not list all the features of the present invention, and various features of the present invention and advantages and effects based on the features can be understood in more detail by referring to the following specific embodiments.
Effects of the invention
According to a preferred aspect of the present invention, an austenitic high manganese steel material excellent in ultra-low temperature toughness and shape and a method for producing the same can be provided.
Drawings
Fig. 1 (a) is a view useful for understanding the valleys and peaks formed on the steel material according to the present invention, and fig. 1 (b) is a photograph taken of the steel material according to an example of the present invention.
Detailed Description
The present invention relates to an austenitic high manganese steel material for ultra-low temperature use excellent in shape and a method for manufacturing the same, and preferred embodiments of the present invention are described hereinafter. The present invention can be variously modified to practice, and the scope of the present invention should not be construed as being limited to the following examples. The following examples are provided to enable those skilled in the art to more fully understand the present invention.
Hereinafter, the steel composition of the present invention will be described in more detail. Unless otherwise specifically indicated, the% indicating the content of each element is based on weight.
The austenitic high-manganese steel material for ultra-low temperature use excellent in shape according to one aspect of the present invention may contain, in weight%: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: greater than 0% and 1% or less, P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance Fe and other unavoidable impurities.
Carbon (C): 0.2 to 0.5 percent
Carbon (C) is not only an element stabilizing austenite but also an effective element ensuring strength by solid solution strengthening. Therefore, in order to secure low-temperature toughness and strength, the present invention may limit the lower limit of the carbon (C) content to 0.2%. That is, if the carbon (C) content is less than 0.2%, austenite that is stable at ultra-low temperatures cannot be obtained due to insufficient stability of austenite, deformation-induced transformation to epsilon-martensite and alpha' -martensite is easily caused by external stress, and toughness and strength of the steel may be reduced. On the other hand, if the carbon (C) content exceeds the predetermined range, the toughness of the steel may be rapidly deteriorated due to precipitation of carbides, the strength of the steel may be excessively high, and the workability of the steel may be significantly reduced, so that the upper limit of the carbon (C) content may be limited to 0.5% in the present invention. Accordingly, the carbon (C) content of the present invention may be 0.2 to 0.5%, preferably 0.3 to 0.5%, and more preferably 0.3 to 0.45%.
Manganese (Mn): 23 to 28 percent
Manganese (Mn) is an element effective for austenite stabilization, and in order to achieve the above-described effects, the present invention may limit the lower limit of the manganese (Mn) content to 23%. That is, since the present invention contains 23% or more of manganese (Mn), the stability of austenite can be effectively increased, thereby inhibiting the formation of ferrite, e-martensite, and a' -martensite, and effectively ensuring the low-temperature toughness of the steel. On the other hand, if the manganese (Mn) content is out of a certain range, the austenite stability increasing effect is saturated, the manufacturing cost is greatly increased, the surface quality may be deteriorated due to excessive internal oxidation during hot rolling, and thus the present invention may limit the upper limit of the manganese (Mn) content to 28%. Therefore, the content of manganese (Mn) in the present invention may be 23 to 28%, and more preferably 23 to 25%.
Silicon (Si): 0.05 to 0.50 percent
Silicon (Si) is an indispensable trace additive element as a deoxidizer, like aluminum (Al). However, if silicon (Si) is excessively added, an oxide is formed on grain boundaries to lower the high-temperature ductility, and there is a possibility that cracks are generated to lower the surface quality, so the upper limit of the silicon (Si) content can be limited to 0.5% in the present invention. On the other hand, since an excessive cost is required to reduce the Si content in steel, the lower limit of the silicon (Si) content may be limited to 0.05% in the present invention. Therefore, the content of silicon (Si) in the present invention may be 0.05 to 0.5%.
Copper (Cu): more than 0% and less than 1%
Copper (Cu) is an element that stabilizes austenite, and is an element that contributes to improvement of low-temperature toughness together with manganese (Mn) and carbon (C). In addition, copper (Cu) is an element having low solid solubility in carbides and diffusing slowly in austenite, and is concentrated at the interface between austenite and carbides to surround the fine carbide nuclei, thereby effectively suppressing the generation and growth of carbides due to further diffusion of carbon (C). Therefore, in order to ensure low-temperature toughness, copper (Cu) must be added in the present invention, and the preferable lower limit of the copper (Cu) content is 0.3%. On the contrary, when the content of copper (Cu) exceeds 1%, hot workability of the steel material is lowered, so the present invention may limit the upper limit of the content of copper (Cu) to 1%. A preferred upper limit of the copper (Cu) content may be 0.8%.
Phosphorus (P): less than 0.03%
Phosphorus (P) is not only an impurity element which is inevitably mixed but also an element which is easily segregated, and is an element which causes cracking or deterioration of weldability at the time of casting. Therefore, in order to prevent deterioration of castability and reduction of weldability, the present invention may limit the upper limit of the content of phosphorus (P) to 0.03%.
Sulfur (S): less than 0.005%
Sulfur (S) is not only an impurity element inevitably mixed but also an element which forms an inclusion to cause hot shortness defects. Therefore, in order to suppress the occurrence of hot shortness, the present invention may limit the upper limit of the sulfur (S) content to 0.005%.
Aluminum (Al): less than 0.5%
Aluminum (Al) is a typical element added as a deoxidizer. However, aluminum (Al) may react with carbon (C) and nitrogen (N) to form precipitates, and the hot workability may be degraded due to the precipitates, so the upper limit of the content of aluminum (Al) may be limited to 0.5% in the present invention. More preferably, the content of aluminum (Al) may be 0.05 to 0.5%.
Chromium (Cr): 2.5 to 4.5 percent
Chromium (Cr) is an element that improves impact toughness at low temperatures by stabilizing austenite and increases the strength of steel by being dissolved in austenite within an appropriate amount of addition range. Chromium is also an element that improves the corrosion resistance of steel. Therefore, in order to achieve the above-described effects, the present invention may add 2.5% or more of chromium (Cr). However, chromium (Cr) is a carbide-forming element and also an element that forms carbide at austenite grain boundaries to reduce low-temperature impact, and the present invention may limit the upper limit of the content of chromium (Cr) to 4.5% in consideration of the content relationship with carbon (C) and other elements added together. Therefore, the chromium (Cr) content of the present invention may be 2.5 to 4.5%, and more preferably, the chromium (Cr) content may be 3 to 4%.
Boron (B): 0.0005 to 0.01%
Boron (B) is a grain boundary strengthening element for strengthening austenite grain boundaries, and can strengthen the austenite grain boundaries even if a small amount of boron (B) is added, so that the high-temperature cracking sensitivity of the steel can be effectively reduced. Therefore, in order to achieve the effects described above, the present invention may limit the lower limit of the boron (B) content to 0.0005%. On the other hand, if the content of boron (B) exceeds the predetermined range, segregation occurs at the austenite grain boundary to increase the high-temperature cracking susceptibility of the steel, and further, the surface quality of the steel may be degraded, so the upper limit of the content of boron (B) may be limited to 0.01% in the present invention. Therefore, the content of boron (B) in the present invention may be 0.0005 to 0.01%, and more preferably 0.002 to 0.006%.
According to one aspect of the present invention, the austenitic high manganese steel for ultra-low temperature use, which is excellent in shape, may contain Fe and other unavoidable impurities as the balance in addition to the above components. However, unexpected impurities from the raw materials or the surrounding environment are inevitably mixed in the conventional manufacturing process, and thus cannot be excluded. Since these impurities are known to any person skilled in the art, not all relevant matters are specifically mentioned in the present description. Also, the addition of other effective ingredients other than the above components is not excluded.
According to one aspect of the present invention, the austenitic high manganese steel for ultra-low temperature use, which is excellent in shape, can effectively ensure the ultra-low temperature toughness of the steel by including austenite of 95 area% or more as a microstructure. The austenite has an average grain size of 5 to 150 μm. The average grain size of austenite that can be achieved in the manufacturing process is 5 μm or more, and if the average grain size is greatly increased, the strength of the steel may be reduced, so the grain size of austenite may be limited to 150 μm or less.
According to one aspect of the present invention, the excellent austenitic high manganese steel for ultra-low temperatures includes carbides and/or e-martensite as an optional structure in addition to austenite. Since the toughness and ductility of the steel may be drastically reduced if the fraction of carbides and/or e-martensite exceeds a certain level, the present invention may limit the fraction of carbides and/or e-martensite to 5 area% or less.
According to one aspect of the present invention, the austenitic high manganese steel for ultra-low temperature use, which is excellent in shape, can have a yield strength of 350MPa or more, a tensile strength of 700MPa or more, and an elongation of 30% or more. In addition, the austenitic high-manganese steel for ultra-low temperature use having excellent shape according to one aspect of the present invention has a Charpy impact toughness at-196 ℃ of 30J or more (based on a thickness of 5 mm), and thus can have excellent ultra-low temperature physical properties.
According to the austenitic high-manganese steel material for ultra-low temperatures having excellent shape of one aspect of the present invention, even if no additional straightening operation or the like is performed after the steel material is manufactured, the difference in height between the peaks and the valleys formed on the steel material in the region of 2m or less with respect to the rolling direction is 10mm or less at most, and therefore, excellent shape uniformity can be ensured. Fig. 1 (a) is a view useful for understanding the valleys and peaks formed on the steel material according to the present invention, and fig. 1 (b) is a photograph taken of the steel material according to an example of the present invention.
Hereinafter, the manufacturing method of the present invention will be described in more detail.
The austenitic high-manganese steel material for ultra-low temperature use excellent in shape according to one aspect of the present invention can be produced by: heating a steel billet once at a temperature ranging from 1050 to 1300 ℃, wherein the steel billet comprises the following components in percentage by weight: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: greater than 0% and 1% or less, P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance of Fe and other unavoidable impurities; performing primary hot rolling of the heated slab at a finish rolling temperature of 800 to 1100 ℃ at a total reduction rate of 35 to 80% to provide an intermediate material; carrying out secondary heating on the intermediate material at the temperature of 1050-1300 ℃; secondarily hot rolling the secondarily heated intermediate material at a finish rolling temperature of (Tnr-120) to Tnr ℃ to provide a hot rolled material; and cooling the hot-rolled material to a temperature range of 600 ℃ or lower at a cooling rate of 1 to 100 ℃/s, and controlling the total reduction ratio of the intermediate material in the temperature range of (Tnr-120) to Tnr ℃ in the secondary hot rolling to 5 to 25%.
One-time heating of steel billet
The composition of the steel slab provided in the manufacturing method of the present invention corresponds to the steel composition of the aforementioned austenitic high manganese steel, and therefore the description of the steel composition of the steel slab is replaced with the description of the steel composition of the aforementioned austenitic high manganese steel.
The steel billet with the steel components can be heated at 1050-1300 ℃ for one time. If the primary heating temperature is lower than the predetermined range, there is a possibility that the rolling load becomes excessive in the primary hot rolling or the alloy components become insufficiently solid-dissolved, so that the lower limit of the primary heating temperature range may be limited to 1050 ℃. On the other hand, if the primary heating temperature is out of the predetermined range, the strength may be reduced due to excessive grain growth, or the hot rolling property of the steel may be deteriorated due to heating beyond the solidus temperature of the steel, so the present invention may limit the upper limit of the primary heating temperature range of the slab to 1300 ℃.
One-pass hot rolling
The primary hot rolling process includes a rough rolling process and a finish rolling process, and the once heated slab can be finish-rolled in the primary hot rolling to be provided as an intermediate material. The total rolling reduction rate of the primary hot rolling can be 35-80%, and the finish rolling of the primary hot rolling is preferably carried out at a temperature range of 800-1100 ℃. If the finish rolling temperature of the primary hot rolling is lower than the predetermined range, an excessive rolling load may be caused when the rolling load is increased, and if the finish rolling temperature of the primary hot rolling is out of the predetermined range, the crystal grains grow coarse and the target strength cannot be obtained.
Primary heating of intermediate material
In order to charge the intermediate material into the heating furnace, the intermediate material may be cut into an appropriate length according to the thickness of the intermediate material, and preferably, the intermediate material may be cut into a length of 1500 to 4000 mm. If the length of the intermediate material is less than 1500mm, tracking in the heating furnace is somewhat difficult, and if the length of the intermediate material exceeds 4000mm, bending may occur in the length direction.
The intermediate material can be heated for the second time within the temperature range of 1050-1300 ℃. If the secondary heating temperature is lower than the predetermined range, there is a possibility that the rolling load in the secondary hot rolling becomes too large or the alloy components are not sufficiently dissolved, so that the lower limit of the secondary heating temperature range may be limited to 1050 ℃. On the other hand, if the reheating temperature is out of the prescribed range, the strength may be reduced due to excessive grain growth, or the hot rolling property of the steel may be deteriorated due to heating beyond the solidus temperature of the steel, so the present invention may limit the upper limit of the reheating temperature range of the intermediate material to 1300 ℃.
Secondary hot rolling
The secondary hot rolling process includes a rough rolling process and a finish rolling process, and the intermediate material subjected to the secondary reheating may be provided as the intermediate material by the secondary hot rolling. In this case, the finish rolling is preferably performed at a temperature ranging from (Tnr-120) to Tnr ℃ wherein Tnr can be derived from the following formula 1.
[ formula 1]
Tnr(℃)＝840+150×C+2.5×Mn+5×Cu+3.5×Cr-50×Si
Wherein C, Mn, Cu, Cr and Si represent the weight% of each component.
If the finish rolling temperature of the secondary hot rolling is lower than (Tnr-120) c, the strength is sharply increased and the impact toughness tends to be deteriorated, while if the finish rolling temperature of the secondary hot rolling exceeds Tnr c, the strength may be decreased due to grain growth, so the present invention can limit the finish rolling temperature of the secondary hot rolling to the range of (Tnr-120) to Tnr c.
In addition, the present invention can control the total reduction of the intermediate material in the temperature range of (Tnr-120) to Tnr ℃ in the secondary hot rolling to 5 to 25%. If the total reduction rate of the intermediate material in the temperature range of (Tnr-120) to Tnr ℃ is less than 5%, the desired shape-correcting effect cannot be achieved, whereas if the total reduction rate of the intermediate material in the temperature range of (Tnr-120) to Tnr ℃ exceeds 25%, the impact toughness may be reduced by excessive pressing.
Cooling down
The hot rolled material after the secondary hot rolling can be cooled to a cooling stop temperature of 600 ℃ or lower at a cooling rate of 1 to 100 ℃/s. If the cooling rate is less than the predetermined range, the carbide precipitated at the grain boundaries during cooling may cause a decrease in the ductility of the steel and thus deterioration in the wear resistance, so that the present invention can limit the cooling rate of the hot-rolled material to 1 ℃/s or more. The lower limit of the preferred cooling rate may be 10 ℃/s and the cooling means may be accelerated cooling. However, although the higher the cooling rate, the more advantageous the carbide precipitation suppressing effect is, the upper limit of the cooling rate may be limited to 100 ℃/s in the present invention considering that the cooling rate exceeding 100 ℃/s in the conventional cooling is difficult to be realized in the equipment characteristics.
Further, even if the hot rolled material is cooled at a cooling rate of 10 ℃/s or more, if the cooling is stopped at a high temperature, the possibility of carbide formation and growth is high, so the present invention can limit the cooling stop temperature to 600 ℃ or less.
The austenitic high manganese steel material thus produced contains 95% by area or more of austenite, and can have a yield strength of 350MPa or more, a tensile strength of 700MPa or more, an elongation of 40% or more, and a Charpy impact toughness of 30J or more (based on a thickness of 5 mm) at-196 ℃.
In addition, the austenitic high manganese steel material thus produced has a difference in height between peaks and valleys formed in a region within 2m in the longitudinal direction of the steel material of at most 10mm, and therefore can ensure excellent shape uniformity.
Modes for carrying out the invention
Hereinafter, the present invention will be described more specifically by examples. It should be noted, however, that the following examples are only intended to illustrate the present invention to be embodied, and are not intended to limit the scope of the present invention.
(examples)
Billets having the alloy compositions of table 1 below and a thickness of 250mm were made. Each billet is heated once at a temperature of 1200 ℃ and then hot rolled once at a finish rolling temperature of 1000 ℃ at a total reduction ratio of 50 to 60% to produce an intermediate material. Hot rolled material samples were produced by performing secondary heating and secondary hot rolling under the conditions of table 2 for each intermediate material, and the yield strength, tensile strength, elongation, charpy impact toughness at-196 ℃ and shape uniformity were measured for each sample and are shown in table 3 below. At this time, the maximum height difference of the peak and the valley formed in the 2m region in the rolling direction of the sample was measured and described for the shape uniformity. Tensile properties were tested at ambient temperature according to ASTM A370, and impact toughness was measured at-196 ℃ after processing to an impact specimen having a thickness of 5mm according to the same specification conditions.
[ TABLE 1]
[ TABLE 2 ]
[ TABLE 3 ]
As shown in tables 2 and 3, the inventive examples satisfying the alloy composition and the manufacturing process of the present invention ensured the physical properties and the shape uniformity to be achieved by the present invention, while the comparative examples not satisfying the alloy composition or the manufacturing process of the present invention failed to ensure the physical properties or the shape uniformity to be achieved by the present invention.
The present invention has been described in detail above by way of examples, but embodiments in different forms may also be adopted. Therefore, the technical spirit and scope of the claims is not limited to the embodiments.
Claims (5)
1. An austenitic high-manganese steel for ultralow temperature use which is excellent in shape,
comprises C: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: greater than 0% and 1% or less, P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance Fe and other unavoidable impurities,
containing 95 area% or more of austenite as a microstructure,
the Charpy impact toughness at-196 ℃ is more than 30J based on the thickness of 5mm,
the difference between the maximum heights of the peaks and valleys formed in the region of 2m or less in the rolling direction is 10mm or less.
2. The austenitic high manganese steel for ultralow temperature use excellent in shape according to claim 1, wherein,
the grain size of the austenite is 5-150 mu m.
3. The austenitic high manganese steel for ultralow temperature use excellent in shape according to claim 1, wherein,
the steel has a yield strength of 350MPa or more, a tensile strength of 700MPa or more, and an elongation of 40% or more.
4. A method for producing an austenitic high-manganese steel material for use at ultra-low temperatures, which has an excellent shape,
heating a steel billet once at a temperature ranging from 1050 to 1300 ℃, wherein the steel billet comprises the following components in percentage by weight: 0.2-0.5%, Mn: 23-28%, Si: 0.05 to 0.5%, Cu: greater than 0% and 1% or less, P: 0.03% or less, S: 0.005% or less, Al: 0.5% or less, Cr: 2.5-4.5%, B: 0.0005 to 0.01%, and the balance of Fe and other unavoidable impurities;
performing primary hot rolling of the heated slab at a finish rolling temperature of 800 to 1100 ℃ at a total reduction rate of 35 to 80% to provide an intermediate material;
carrying out secondary heating on the intermediate material at the temperature of 1050-1300 ℃;
secondarily hot rolling the secondarily heated intermediate material at a finish rolling temperature of (Tnr-120) to Tnr ℃ to provide a hot rolled material;
cooling the hot rolled material to a temperature range below 600 ℃ at a cooling rate of 1-100 ℃/s,
in the secondary hot rolling, the total reduction rate of the intermediate material at a temperature ranging from (Tnr-120) to Tnr ℃ is 5 to 25%.
5. The method for producing an austenitic high-manganese steel material for ultralow temperature use excellent in shape according to claim 5, wherein said austenite high-manganese steel material for ultralow temperature use is a steel material for ultralow temperature use,
in the hot rolled material after finishing cooling, the difference between the maximum heights of the peaks and valleys formed in the region of 2m or less in the rolling direction is 10mm or less.
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| KR10-2019-0118925 | 2019-09-26 | ||
| KR1020190118925A KR102255826B1 (en) | 2018-10-25 | 2019-09-26 | Ultra-low temperature austenitic high manganese steel having excellent shape and manufacturing method for the same |
| PCT/KR2019/014193 WO2020085861A1 (en) | 2018-10-25 | 2019-10-25 | Cryogenic austenitic high-manganese steel having excellent shape, and manufacturing method therefor |
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| WO2017111510A1 (en) * | 2015-12-23 | 2017-06-29 | 주식회사 포스코 | Non-magnetic steel material having excellent hot workability and manufacturing method therefor |
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| KR101899692B1 (en) * | 2016-12-23 | 2018-09-17 | 주식회사 포스코 | Low temperature austenitic high manganese steel and method for manufacturing the same |
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| CN107881432A (en) * | 2017-10-13 | 2018-04-06 | 舞阳钢铁有限责任公司 | Inexpensive ultralow temperature steel heavy plate for pressure vessels and its production method |
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| JP2007126715A (en) * | 2005-11-04 | 2007-05-24 | Sumitomo Metal Ind Ltd | HIGH-Mn STEEL MATERIAL AND MANUFACTURING METHOD THEREFOR |
| CN104220617A (en) * | 2011-12-27 | 2014-12-17 | Posco公司 | Austenitic steel having superior machinability and cryogenic temperature toughness in weld heat affected zones thereof and method for manufacturing same |
| CN106222554A (en) * | 2016-08-23 | 2016-12-14 | 南京钢铁股份有限公司 | A kind of economical steel used at ultra-low temperature and preparation method thereof |
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