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WO2018124654A1 - Acier au manganèse moyen à haute résistance pour estampage à chaud et son procédé de fabrication - Google Patents

Acier au manganèse moyen à haute résistance pour estampage à chaud et son procédé de fabrication Download PDF

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Publication number
WO2018124654A1
WO2018124654A1 PCT/KR2017/015341 KR2017015341W WO2018124654A1 WO 2018124654 A1 WO2018124654 A1 WO 2018124654A1 KR 2017015341 W KR2017015341 W KR 2017015341W WO 2018124654 A1 WO2018124654 A1 WO 2018124654A1
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Prior art keywords
temperature
weight
manganese steel
composition
warm
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Ceased
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PCT/KR2017/015341
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English (en)
Korean (ko)
Inventor
이영국
한정호
남재훈
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Industry Academic Cooperation Foundation of Yonsei University
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Industry Academic Cooperation Foundation of Yonsei University
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Priority claimed from KR1020170177216A external-priority patent/KR102030815B1/ko
Application filed by Industry Academic Cooperation Foundation of Yonsei University filed Critical Industry Academic Cooperation Foundation of Yonsei University
Priority to US16/760,263 priority Critical patent/US11566306B2/en
Publication of WO2018124654A1 publication Critical patent/WO2018124654A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese

Definitions

  • the present invention relates to high strength medium manganese steel. Specifically, the present invention relates to a high strength intermediate manganese steel for warm forming and a method of manufacturing the same.
  • an ultra high strength steel sheet having a tensile strength of 980 MPa or more is used, and should have high elongation as well as high strength.
  • research on commercialization of high strength steel is increasing as the ratio of using high strength steel increases.
  • the prior art hot stamping process has several problems.
  • the boron-added steel cannot obtain a hard martensite structure unless it is quenched after molding.
  • water is flowed into the mold to cool it rapidly while keeping the specimen as it is in the mold. This not only lowers the productivity of the process, but also causes the mold surface to suffer from heat fatigue due to repeated heating and cooling.
  • Patent Document 1 (Document 1) Korea Patent Registration No. 10-0765723 (2007.10.02)
  • Patent Document 2 (Document 2) Korean Unexamined Patent Publication No. 10-2013-0050138 (2013.05.15)
  • the high strength medium manganese steel for warm forming and the method of manufacturing the same according to the present invention have the following problems.
  • the high strength medium manganese steel for warm forming according to the present invention contains components of manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight. It is preferred to be composed of iron and iron (Fe) and inevitably contained impurities.
  • niobium (Nb) 0.001-0.1% by weight is further contained in the medium manganese steel.
  • the aluminum manganese steel further contains 0.001-5.0% by weight of aluminum (Al).
  • At least one member selected from the group consisting of chromium (Cr), molybdenum (Mo), nickel (Ni) and titanium (Ti) is 0.001-2.0 wt% It is preferable to contain more.
  • the high strength medium manganese steel forming member for warm forming contains components of manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight.
  • the high strength medium manganese steel forming member for warm forming according to the present invention contains components of manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight.
  • T 50 the sum of the volume fractions of tempered martensite, bainite and ferrite is preferably 50% or more.
  • the high strength medium manganese steel forming member for warm forming contains components of manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight. in the composition or the composition containing glass denied iron (Fe) and inevitable impurities, niobium (Nb): 0.001 to 0.1 of a composition further contains the components of the% by weight of ferrite and austenite or more reverse Ac 3 At temperature, Ac 3 After the austenizing process in the second temperature section from the temperature to 100 °C, it is preferable that the volume fraction of martensite is 90% or more.
  • the yield strength of the high strength medium manganese steel forming member for warm forming according to the present invention is preferably 1.0 GPa or more, and tensile strength is 1.5 GPa or more.
  • the method for manufacturing a high strength medium manganese steel forming member for warm forming comprises manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight S3 step of preparing a hot-rolled steel sheet or a cold-rolled steel sheet containing a composition containing the remaining iron (Fe) and unavoidable impurities, or the composition further contains niobium (Nb): 0.001-0.1% by weight of the component; Ac 3 at a temperature which is 1 (T 50): 1 and Ac 3 -Ac than the ferrite and austenite in the first station 1st temperature range up to temperature or Ac 3 It is preferable to include the step S4 of performing austenizing while maintaining a predetermined time after heating the hot-rolled steel sheet or the cold-rolled steel sheet in a second temperature section from a temperature to 100 °C.
  • the intermediate manganese steel slab having the composition is reheated for a predetermined time at 1000-1200 ° C., which is a temperature section of the austenitic single phase region, and Ac 3 Ms temperature ⁇ Ac 3 after hot finish rolling at temperature above 1000 °C It is preferable to further include an S1 step of producing a hot rolled steel sheet by winding at a temperature.
  • step S1 In the method for manufacturing a high strength medium manganese steel forming member for warm forming according to the present invention, after the step S1 and before the step S3, it is preferable to further include the step S2 of performing cold rolling at room temperature to produce a cold rolled steel sheet.
  • step S3-1 before annealing the hot rolled steel sheet or the cold rolled steel sheet.
  • the method for manufacturing a high strength intermediate manganese steel forming member for warm forming according to the present invention preferably includes a step S5-1 of performing warm forming in a temperature section of step S4 after the austenizing.
  • the method for manufacturing a high strength intermediate manganese steel forming member for warm forming according to the present invention preferably includes a step S5-2 after performing austenizing and performing warm forming at a temperature lower than 10-300 ° C. than the austenizing temperature.
  • the method for manufacturing a high strength medium manganese steel forming member for warm forming according to the present invention is heated to 1-100 ° C./sec to the warm forming temperature, and is press-molded after holding at 10-1000 sec, followed by a speed of 1 to 30 ° C./sec. Slow cooling is preferred.
  • the high-strength medium manganese steel for warm forming according to the present invention and its manufacturing method have the following effects.
  • the heat energy is reduced by heat treatment of the high heat energy consumption of the existing hot stamping process at low austenizing temperature of the middle manganese steel.
  • Example 1 is a graph showing the tensile properties according to the heat treatment temperature after cold rolling of the specimen of Example 1 according to the present invention.
  • Example 2 is a graph showing the tensile properties according to the heat treatment temperature after cold rolling annealing the specimen of Example 1 according to the present invention.
  • Example 3 is a graph showing the tensile properties according to the heat treatment temperature after cold rolling of the specimen of Example 2 according to the present invention.
  • Figure 4 is a photograph showing the microstructure between the tempered martens formed during slow cooling after the hot rolling and winding process of Example 1 according to the present invention.
  • Example 5 is a graph showing the hardness value according to the presence or absence of the winding process after hot rolling of Example 1 according to the present invention.
  • Figure 6 shows a method of manufacturing a high-strength medium manganese steel forming member for warm molding according to the present invention.
  • the high strength medium manganese steel for warm forming according to the present invention contains components of manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight. It is preferred to be composed of iron and iron (Fe) and inevitably contained impurities.
  • the alloy of the present invention comprises Mn: 3-10% by weight, C: 0.05-0.3% by weight, Si: 0.1-0.5% by weight and is composed of the remaining Fe and other unavoidable impurities.
  • a small amount of alloying elements Nb is included at 0.001-0.1% by weight.
  • the steel sheet may additionally contain 0.001-5.0 wt% of one or more selected from the group consisting of Cr, Mo, Ni, Al, and Ti.
  • the 3-10% by weight Mn content improves the stability of austenite at high temperatures, suppresses ferrite transformation during cooling, and thus martensite structure can be obtained even in slow cooling.
  • the press molding temperature can be lowered by lowering the dual-phase zone temperature.
  • Mn content is less than 3% by weight, austenite stability is poor, and ferrite may be generated during cooling after hot rolling, and may exhibit martensite-ferrite abnormality at room temperature.
  • Mn content exceeds 10% by weight, not only the increase in raw material cost and manufacturing cost but also a problem in that the weldability is lowered and a large amount of manganese sulfide (MnS) is formed. Therefore, in the present invention, it is preferable to limit the Mn content to 3-10% by weight.
  • the C content of 0.05-0.3% by weight can ensure the stability of the austenite at high temperatures, and can be dissolved in martensite at room temperature to improve strength.
  • the C content is less than 0.05% by weight, there is a possibility that austenite is less stable and ferrite is formed during cooling, and the strength of the martensite internal solid solution C is lowered.
  • the C content is more than 0.3% by weight, there is a possibility that the cold rolling property after the hot rolling is less than the strength, the weldability may be lowered. Therefore, in the present invention, it is preferable to limit the C content to 0.05-0.3% by weight.
  • Si is a ferrite stabilizing element, it increases the austenite hardenability at high temperatures to suppress ferrite transformation during cooling. It also inhibits carbide formation during cooling and accelerates C segregation to austenite in ferrite-austenite anomalies.
  • Si is less than 0.1% by weight, the solid solution strengthening effect of Si is reduced and the diffusion of carbon into austenite becomes difficult.
  • Si content exceeds 1.0% by weight, problems such as an increase in raw material costs and manufacturing costs, continuous casting, difficulty in welding and plating, and the like may occur. Therefore, in the present invention, it is preferable to limit the Si content to 0.1-1.0% by weight.
  • Nb is an element that enhances the strength of steel sheet, refines grains, and improves heat treatment properties by depositing a solid solution effect and solid solution carbon.
  • the content of the element is less than 0.001% by weight, the amount of precipitated niobium carbide (NbC) is small and it is difficult to expect the effect of improving the strength.
  • the content of the element exceeds 0.1% by weight, the excessive manufacturing cost rises. Therefore, it is preferable to limit the content to 0.001-0.1% by weight.
  • Al deoxidizes and is added as an element which improves the cleanliness of steel and suppresses carbide generation.
  • the abnormal region may be expanded to perform uniform heat treatment, but if it exceeds 5.0% by weight, the abnormal region temperature is increased, and the low austenizing temperature of the present invention is increased again. Higher stability may result in the presence of ferrite at room temperature after molding.
  • the plating property of the steel sheet is lowered and the manufacturing cost is increased. Therefore, in the present invention, it is preferable to limit the Al content to 0.001-5.0% by weight.
  • Cr, Mo, Ti, and Ni are hardening elements and precipitation strengthening effects, and are elements having a large effect to further secure high strength. If it is less than 0.001 weight%, sufficient hardenability and precipitation strengthening effect are hard to expect, and when it exceeds 2.0 weight%, manufacturing cost will rise. Therefore, in the present invention, it is preferable to limit the content to 0.001-2.0% by weight.
  • Niobium (Nb) addition manganese steel manufacturing method for warm stamping includes hot rolling and cold rolling conditions, blank forming step, blank heating and forming step, blank cooling step. do.
  • the cast ingot is homogenized for 12 hours at 1000-1400 °C for uniform alloy element distribution in the steel. If the said heating temperature is less than 1000 degreeC, the homogenization of performance structure will not fully be ensured. If it exceeds 1400 ° C., an increase in manufacturing cost occurs.
  • Hot finish rolling shall be performed at the temperature of Ac 3 , which is the transformation critical temperature, at 1000 ° C. or lower during heating. Thereafter, the annealed wound in more than Ac 3 temperature below Ms (martensite start temperature generated).
  • austenite begins to transform martensite as it passes Ms.
  • martensite is a body-centered tetragonal (bct) crystal structure with many dislocations formed therein, and carbon diffusion is accelerated. Therefore, cementite precipitates inside martensite during slow cooling.
  • the final microstructure consists of two phases of tempered martensite and bainite, or three phases of tempered martensite, bainite and ferrite. In the three phases, the volume fraction of ferrite is preferably 10% or less (0% not included). The tissue photograph and hardness test results of the three phases are shown in FIG. 4.
  • ferrite In the austenizing heat treatment, ferrite remains at a temperature of Ac 3 or lower, and the final normal temperature strength is lowered. Through the above process, it is possible to improve the cold rolling property by lowering the strength of the hot rolled steel sheet.
  • the hot rolled plate may be additionally cold rolled at room temperature to produce a cold rolled steel sheet.
  • the cold rolled steel sheet may then comprise an annealing heat treatment at 550-750 ° C. for 1 minute-5 minutes.
  • the steel sheet is cut to form a blank.
  • This blank is designed to fit the mold shape.
  • the heat treatment temperature was proposed as an Ac 1 -Ac 3 or higher region temperature.
  • a low molding temperature strength corresponding to a hot stamping steel was not obtained.
  • the composition and content of the present invention such as essentially containing aluminum (Al)
  • Al does not produce sufficient austenite at the heat treatment temperature, and thus sufficient martensite is not produced during cooling after molding, thereby securing a target strength. It is judged that it was difficult.
  • the high-strength steel having a high elongation in the first temperature range from the temperature (T 50 ) at which the volume fraction of ferrite and austenite becomes 1: 1 in the Ac 1 -Ac 3 or higher region to Ac 3 temperature and a second temperature range of from Ac 3 temperature to 100 °C a temperature above the Ac 3 temperature is designated the ultra-high strength in the age ranging austenite temperature range of interest.
  • the heated steel sheet After the austenizing process, the heated steel sheet is transferred to a mold for warm forming at a temperature 10-300 ° C. lower than the austenizing temperature.
  • a mold When transferring to a mold, it is inevitable that the temperature of the heated steel sheet falls below 10 ° C., and when the temperature falls below 300 ° C., the yield strength of the steel sheet increases, and a large load is applied to the mold during molding. This leads to an increase in the life of the mold and the manufacturing cost.
  • the heated blank is transferred to a press die for press molding, and then the molded parts are taken out and cooled in air.
  • quenching is required in a mold to obtain martensite, but the inventive steel can obtain martensite structure even at a slow cooling rate such as air cooling.
  • the microstructure of the formed steel sheet exhibits martensite, bainite, ferrite, austenite multiphase structure. Martensite and bainite in the first temperature range. Ferrites, the sum of their volume fractions is at least 50%. When the austenite volume fraction is T50, the stability of the austenite becomes 20% or more. In the second temperature section, the steel sheet has a volume fraction of martensite of 90% or more.
  • the cold rolled sheet thus manufactured was used to simulate the heat treatment conditions of the warm stamping process.
  • the ferrite and austenite were 1: 1 at a temperature ranging from T 50 to austenite single phase region temperature range of 50 ° C. higher than A 3 .
  • the temperature increase rate is 3 °C / second and the cooling rate is 10 °C / second.
  • inventive steels A-1 to A-3 exhibit excellent room temperature tensile properties when the heat treatment is performed at a temperature of about 10-50 degrees or more than the A 3 temperature.
  • invented steels A-4 to A-7 which are lower than A 3 temperature, do not reach the yield strength and tensile strength (TS) required as a hot stamping replacement steel.
  • Invented steel A-7 can be applied to parts requiring high yield strength and elongation index (EI).
  • EI elongation index
  • Inventive steels B and C also exhibit excellent physical properties when subjected to austenizing heat treatment above the A 3 temperature.
  • Tensile curves according to the respective heat treatment temperatures of the inventive steels B and C are shown in FIGS. 2 and 3, respectively.
  • the austenitic fraction of the final microstructure at room temperature after air cooling according to temperature is shown in Table 5 below. The lower the temperature, the higher the stability of the reverse-transformed austenite and the residual austenite fraction increased.
  • Inventive steel A-3 heat-treated above the A3 temperature indicates that no residual austenite is present, and all of the reverse austenite is transformed into martensite. Therefore, room temperature yield and tensile strength are excellent.
  • the yield and tensile strength of the inventive steel A increased without decreasing the elongation of the inventive steel B at the same heat treatment temperature. It can be confirmed that the strength due to the solid solution strengthening and precipitation strengthening by adding Nb is improved.
  • Inventive steel A which was cold rolled in Example 1, was further subjected to annealing heat treatment (CA).
  • the heat treatment conditions were performed while changing the temperature to 650-750 ° C 3 minutes.
  • the cold-rolled steel sheet was processed by subdividing the heat treatment conditions of the warm stamping process into an austenizing temperature (T A ) and a molding temperature (T S ).
  • the austenizing temperature was 650-750 o C for 5 minutes and the molding temperature was 650-750 o C for 1 minute.
  • air was cooled to room temperature. At this time, the temperature increase rate is 3 o C / sec and the cooling rate is 10 o C / sec.
  • the annealing temperature (CA) and the molding temperature (T S ) was confirmed that does not significantly affect the room temperature tensile properties. Similar to Example 1, the austenizing temperature (T A ) has a large effect. Inventive steel A-8 to invention steel A-11, invention steel A-18 to invention steel A-21, and invention steel A-28 to invention steel A-31 all exhibited superior physical properties than hot stamping steel. have. At low T A , the target tensile temperature was not reached.
  • Example 3 unlike Example 1 and Example 2, the inventive steel A was advanced to a hot rolled steel sheet without cold rolling.
  • Invented steel A-38 and Invented steel A-39 were subjected to annealing heat treatment at 750 ° C. for 3 minutes. Thereafter, the steel sheet was further divided into heat treatment conditions of a warm stamping process into an austenizing temperature (T A ) and a molding temperature (T S ).
  • the austenizing temperature was varied by changing the temperature to 650-750 ° C. for 5 minutes and the molding temperature to 600 ° C. for 1 minute.
  • air was cooled to room temperature. At this time, the temperature increase rate is 3 °C / second and the cooling rate is 10 ° C / second.
  • the annealing temperature (CA) and the forming temperature (T S ) was confirmed that does not significantly affect the room temperature tensile properties. Similar to Examples 1 and 2, the austenizing temperature (T A ) has a large effect. Invented steel A-38 and invented steel A-40 all exhibit superior physical properties than hot stamping steel. At low T A , the target tensile temperature was not reached. Through the above embodiment, it was confirmed that the hot stamping steel sheet can be applied as a hot stamping steel sheet to replace the hot stamping steel sheet without the hot rolling process.
  • Figure 6 shows a method of manufacturing a high strength intermediate manganese steel forming member for warm molding according to the present invention.
  • One manufacturing method according to the invention comprises at least S3 step and S4 step.
  • Step S3 contains components of manganese (Mn): 3-10% by weight, carbon (C): 0.05-0.3% by weight and silicon (Si): 0.1-1.0% by weight, and the balance of iron (Fe) ) And a hot rolled steel sheet or a cold rolled steel sheet having a composition containing an unavoidable impurity or a composition further containing a component of niobium (Nb): 0.001-0.1% by weight.
  • step S3 all compositions of FMS according to the present invention can be applied.
  • a cold rolled steel sheet subjected to hot rolling and cold rolling may be applied, or a hot rolled steel sheet roughly subjected to hot rolling may be applied.
  • the intermediate manganese steel slab having the composition is reheated for a predetermined time at 1000-1200 ° C., which is a temperature section of the austenitic single phase region, and subjected to hot finishing rolling at an Ac 3 temperature or more and 1000 ° C. or lower, and then, an Ms temperature.
  • ⁇ Ac 3 It can be wound at a temperature to produce a hot rolled steel sheet.
  • S2 step according to the present invention can be produced by cold rolling at room temperature cold rolling.
  • it may further comprise a S3-1 step of annealing the hot rolled steel sheet or the cold rolled steel sheet.
  • Step S4 is Ac 1 -Ac 3 above reverse the ferrite and austenite 1 at a temperature (T 50) is the first Ac 3 1st temperature range up to temperature or Ac 3 After heating the hot rolled steel sheet or the cold rolled steel sheet in a second temperature section from a temperature to 100 ° C., austenizing may be performed while maintaining a predetermined time.
  • after the austenizing may include a step S5-1 performing the warm molding in the temperature section of the step S4.
  • FIG. 7 shows that steps S4 and S5-1 are performed in the second temperature section
  • FIG. 8 shows that steps S4 and S5-1 are performed in the second temperature section.
  • step S5-2 to perform the warm molding at a temperature 10-300 °C lower than the austenizing temperature.
  • 9 shows that step S4 is performed in the first temperature section
  • step S5-2 is performed in the lower temperature section
  • FIG. 10 shows step S4 is performed in the first temperature section, and in the lower temperature section. Indicates that step S5-2 is performed.
  • the present invention can obtain martensite structure by slow cooling such as air cooling after warm forming.

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Abstract

La présente invention concerne de l'acier au manganèse moyen à haute résistance, pour l'estampage à chaud, contenant de 3 à 10 % en poids de manganèse (Mn), de 0,05 à 0,3 % en poids de carbone (C) et de 0,1 à 1,0 % en poids de silicium (Si), le reste étant constitué de fer (Fe) et des impuretés inévitables. La présente invention permet de réduire la consommation élevée d'énergie thermique d'une technique d'estampage à chaud existante au moyen d'un traitement thermique à une température d'austénitisation faible de l'acier au manganèse moyen. De plus, étant donné que la présente invention ne nécessite pas d'opération de malaxage supplémentaire et permet l'acquisition d'une haute résistance simplement au moyen d'un refroidissement lent, tel qu'un refroidissement par air à l'extérieur d'un moule sans refroidissement rapide dans le moule, la technique est simplifiée et la productivité est améliorée.
PCT/KR2017/015341 2016-12-28 2017-12-22 Acier au manganèse moyen à haute résistance pour estampage à chaud et son procédé de fabrication Ceased WO2018124654A1 (fr)

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US16/760,263 US11566306B2 (en) 2016-12-28 2017-12-22 High-strength medium manganese steel for warm stamping and method for manufacturing same

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KR10-2016-0180900 2016-12-28
KR20160180900 2016-12-28
KR10-2017-0177216 2017-12-21
KR1020170177216A KR102030815B1 (ko) 2016-12-28 2017-12-21 온간성형용 고강도 중망간강 성형부재와 그 제조방법

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CN113840936A (zh) * 2019-05-31 2021-12-24 日本制铁株式会社 热冲压成型体
CN114107813A (zh) * 2021-11-22 2022-03-01 北京科技大学 一种马氏体+奥氏体双相中锰铸钢及制备方法

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KR101677398B1 (ko) * 2015-11-30 2016-11-18 주식회사 포스코 열간성형용 강재 및 이를 이용한 부재 제조방법
CN106086653A (zh) * 2016-08-15 2016-11-09 大连理工大学 一种实现性能梯度、等厚度的温热成形中锰钢件制备方法

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CN113840936B (zh) * 2019-05-31 2022-06-17 日本制铁株式会社 热冲压成型体
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