US20220213573A1 - A cold rolled martensitic steel and a method of martensitic steel thereof - Google Patents
A cold rolled martensitic steel and a method of martensitic steel thereof Download PDFInfo
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- US20220213573A1 US20220213573A1 US17/610,906 US202017610906A US2022213573A1 US 20220213573 A1 US20220213573 A1 US 20220213573A1 US 202017610906 A US202017610906 A US 202017610906A US 2022213573 A1 US2022213573 A1 US 2022213573A1
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- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
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- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
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- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a method of manufacturing of a cold rolled martensitic steel suitable for automotive industry and particularly to Martensitic steels having tensile strength 1280 MPa or more.
- Automotive parts are required to satisfy two inconsistent necessities, namely ease of forming and strength but in recent years a third requirement of improvement in fuel consumption is also bestowed upon automobiles in view of global environment concerns.
- automotive parts must be made of material having high formability in order that to fit in the criteria of ease of fit in the intricate automobile assembly and at same time have to improve strength for vehicle crashworthiness and durability while reducing the weight of the vehicle to improve fuel efficiency.
- the steel sheet of WO2017/065371 is manufactured through the steps of: rapidly heating a material steel sheet for 3 to 60 seconds to an Ac3 transformation point or higher and maintaining the material steel sheet, the material steel sheet containing 0.08 to 0.30 wt % of C, 0.01 to 2.0 wt % of Si, 0.30 to 3.0 wt % of Mn, 0.05 wt % or less of P and 0.05 wt % or less of S and the remainder being Fe and other unavoidable impurities; rapidly cooling the heated steel sheet to 100° C./s or higher with water or oil; and rapidly tempering to 500° C. to Al transformation point for 3 to 60 seconds including heating and maintaining time.
- the steel of WO2017/065371 not able to surpass the tensile strength of 1300 MPa and do not mention about hole expansion ratio even having a tempered martensite single phase structure.
- WO2010/036028 relates to a hot dip galvanized steel sheet and a manufacturing method thereof.
- the hot dip galvanize steel sheet includes a steel sheet including a martensitic structure as a matrix, and a hot dip galvanized layer formed on the steel sheet.
- the steel sheet includes C of 0.05 wt % to 0.30 wt %, Mn of 0.5 wt % to 3.5 wt %, Si of 0.1 wt % to 0.8 wt %, Al of 0.01 wt % to 1.5 wt %, Cr of 0.01 wt % to 1.5 wt %, Mo of 0.01 wt % to 1.5 wt %, Ti of 0.001 wt % to 0.10 wt %, N of 5 ppm to 120 ppm, B of 3 ppm to 80 ppm, an impurity, and the remainder of Fe.
- the steel of WO2010/036028 does not mentions hole expansion ratio.
- such steel can also have a good suitability for forming, for rolling with good weldability and coatability.
- the present invention provides a cold rolled martensitic steel sheet comprising of the following elements, expressed in percentage by weight: 0.1% ⁇ C ⁇ 0.2%; 1.5% ⁇ Mn ⁇ 2.5%; 0.1% ⁇ Si ⁇ 0.25%; 0.1% ⁇ Cr ⁇ 1%; 0.01% ⁇ Al ⁇ 0.1%; 0.001% ⁇ Ti ⁇ 0.1%; 0% ⁇ S ⁇ 0.09%; 0% ⁇ P ⁇ 0.09%; 0% ⁇ N ⁇ 0.09%; and can contain one or more of the following optional elements 0% ⁇ Ni ⁇ 1%; 0% ⁇ Cu ⁇ 1%; 0% ⁇ Mo ⁇ 0.4%; 0% ⁇ Nb ⁇ 0.1%; 0% ⁇ V ⁇ 0.1%; 0% ⁇ B ⁇ 0.05%; 0% ⁇ Sn ⁇ 0.1%; 0% ⁇ Pb ⁇ 0.1%; 0% ⁇ Sb ⁇ 0.1%; 0.001% ⁇ Ca ⁇ 0.01%; the remainder composition being composed of iron and unavoidable impurities caused by processing, the microstructure of said steel comprising, by area percentage, at least 95% of martensite, a cumulated amount of fer
- Another object of the present invention is also to make available a method for the manufacturing of these sheets that is compatible with conventional industrial applications while being robust towards manufacturing parameters shifts.
- the chemical composition of the cold rolled martensitic steel comprises of the following elements:
- Carbon is present in the steel of the present invention is between 0.1% and 0.2%. Carbon is an element necessary for increasing the strength of the Steel of the present invention by producing low-temperature transformation phases such as Martensite. Therefore, Carbon plays two pivotal roles, one is to increase the strength. Carbon content less than 0.1% will not be able to impart the tensile strength to the steel of the present invention. On the other hand, at a Carbon content exceeding 0.2%, the steel exhibits poor spot weldability which limits its application for the automotive parts. A preferable content for the present invention may be kept between 0.11% and 0.19% and more preferably between 0.12% and 0.18%.
- Manganese content of the steel of the present invention is between 1.5% and 2.5%. This element is gammagenous. Manganese provides solid solution strengthening and suppresses the ferritic transformation temperature and reduces ferritic transformation rate hence assist in the formation of martensite. An amount of at least 1.5% is required to impart strength as well as to assist the formation of Martensite. But when Manganese content is more than 2.5% it produces adverse effects such as it retards transformation of Austenite to Martensite during cooling after annealing. Manganese content of above 2.5% can get excessively segregated in the steel during solidification and homogeneity inside the material is impaired which can cause surface cracks during a hot working process. The preferred limit for the presence of Manganese is between 1.6% and 2.4% and more preferably between 1.6% and 2.2%.
- Silicon content of the steel of the present invention is between 0.1% and 0.25%.
- Silicon is an element that contributes to increasing the strength by solid solution strengthening. Silicon is a constituent that can retard the precipitation of carbides during cooling after annealing, therefore, Silicon promotes formation of Martensite. But Silicon is also a ferrite former and also increases the Ac3 transformation point which will push the annealing temperature to higher temperature ranges, which is why the content of Silicon is kept at a maximum of 0.25%. Silicon content above 0.25% can also temper embrittlement and in addition silicon also impairs coatability.
- the preferred limit for the presence of Silicon is between 0.16% and 0.24% and more preferably between 0.18% and 0.23%.
- Chromium content of the steel of the present invention is between 0.1% and 1%. Chromium is an essential element that provide strength to the steel by solid solution strengthening and a minimum of 0.1% is required to impart the strength but when used above 1% impairs surface finish of steel. The preferred limit for the presence of Chromium is between 0.1% and 0.5%.
- the content of Aluminum is between 0.01% and 1% in the present invention.
- Aluminum removes Oxygen existing in molten steel to prevent Oxygen from forming a gas phase during the solidification process.
- Aluminum also fixes Nitrogen in the steel to form Aluminum nitride to reduce the size of the grains.
- Higher content of Aluminum, above 1%, increases Ac3 point to a high temperature thereby lowering the productivity.
- the preferred limit for the presence of Aluminium is between 0.01% and 0.05%
- Titanium is added to the Steel of the present invention between 0.001% to 0.1%. It forms Titanium-nitrides appearing during solidification of the cast product.
- the amount of Titanium is so limited to 0.1% to avoid the formation of coarse Titanium-nitrides detrimental for formability. Titanium content below 0.001% does not impart any effect on the steel of the present invention.
- Sulfur is not an essential element but may be contained as an impurity in steel and from the point of view of the present invention the Sulfur content is preferably as low as possible but 0.09% or less from the viewpoint of manufacturing cost. Further if higher Sulfur is present in the steel it combines to form Sulfides especially with Manganese and reduces its beneficial impact on the present invention.
- Phosphorus constituent of the Steel of the present invention is between 0% and 0.09%, Phosphorus reduces the spot weldability and the hot ductility, particularly due to its tendency to segregate at the grain boundaries or co-segregate with Manganese. For these reasons, its content is limited to 0.09% and preferably lower than 0.06%.
- Nitrogen is limited to 0.09% to avoid ageing of material and to minimize the precipitation of Aluminum nitrides during solidification which are detrimental for mechanical properties of the steel.
- Molybdenum is an optional element that constitutes 0% to 0.4% of the Steel of the present invention. Molybdenum plays an effective role in improving hardenability and hardness, delays the appearance of Bainite hence promotes the formation of Martensite, in particular when added in an amount of at least 0.001% or even of at least 0.002%. However, the addition of Molybdenum excessively increases the cost of the addition of alloy elements, so that for economic reasons its content is limited to 0.4%.
- Niobium is present in the Steel of the present invention between 0% and 0.1% and suitable for forming carbo-nitrides to impart strength of the Steel of the present invention by precipitation hardening. Niobium will also impact the size of microstructural components through its precipitation as carbo-nitrides and by retarding the recrystallization during the heating process. Thus, finer microstructure formed at the end of the holding temperature and as a consequence after the complete annealing will lead to the hardening of the product. However, Niobium content above 0.1% is not economically interesting as a saturation effect of its influence is observed this means that additional amount of Niobium does not result in any strength improvement of the product.
- Vanadium is effective in enhancing the strength of steel by forming carbides or carbo-nitrides and the upper limit is 0.1% from economic points of view.
- Nickel may be added as an optional element in an amount of 0% to 1% to increase the strength of the steel present invention and to improve its toughness. A minimum of 0.01% is preferred to get such effects. However, when its content is above 1%, Nickel causes ductility deterioration.
- Copper may be added as an optional element in an amount of 0% to 1% to increase the strength of the steel of the present invention and to improve its corrosion resistance. A minimum of 0.01% is preferred to get obtain such effects. However, when its content is above 1%, it can degrade the surface aspects.
- Boron is an optional element for the steel of the present invention and may be present between 0% and 0.05%. Boron forms boro-nitrides and impart additional strength to the steel of the present invention when added in an amount of at least 0.0001%.
- Calcium can be added to the steel of the present invention in an amount between 0.001% and 0.01%. Calcium is added to the steel of the present invention as an optional element especially during the inclusion treatment. Calcium contributes towards the refining of the Steel by binding the detrimental Sulfur content in globular form thereby retarding the harmful effect of Sulfur.
- Sn, Pb or Sb can be added individually or in combination in the following proportions: Sn ⁇ 0.1%, Pb ⁇ 0.1% and Sb ⁇ 0.1%. Up to the maximum content levels indicated, these elements make it possible to refine the grain during solidification.
- the remainder of the composition of the steel consists of iron and inevitable impurities resulting from processing.
- Martensite constitutes at least 95% of the microstructure by area fraction.
- the martensite of the present invention can comprise both fresh and tempered martensite.
- fresh martensite is an optional microconstituent which is limited in the steel at an amount of between 0% an 4%, preferably between 0 and 2% and even better equal to 0%.
- Fresh martensite may form during cooling after tempering. Tempered martensite is formed from the martensite which forms during the second step of cooling after annealing and particularly after the cooling is below Ms temperature and more particularly between Ms-10° C. and 20° C. Such martensite is then tempered during the holding at a tempering temperature Ttemper between 150° C. and 300° C.
- the martensite of the present invention imparts ductility and strength to such steel.
- the content of martensite is between 96% and 99% and more preferably between 97% and 99%.
- the cumulated amount of ferrite and bainite represents between 1% and 5% of the microstructure.
- the cumulative presence of bainite and ferrite does not affect adversely to the present invention until 5% but above 5% the mechanical properties may be impacted adversely.
- the preferred limit for the cumulative presence ferrite and bainite is kept between 1% and 4% and more preferably between 1% and 3%.
- Bainite forms during the reheating before tempering.
- the steel of present invention contains 1 to 3% of bainite. Bainite can impart formability to the steel but when present in too large an amount, it may adversely impact the tensile strength of the steel.
- Ferrite may form during the first step of cooling after annealing but is not required as a microstructural constituent. Ferrite formation must be kept as low as possible and preferably less than 2% or even less than 1%.
- Residual Austenite is an optional microstructure that can be present between 0% and 2% in the steel.
- the microstructure of the cold rolled martensitic steel sheet is free from microstructural components such as pearlite and cementite.
- the steel according to the invention can be manufactured by any suitable methods. It is however preferable to use the method according to the invention that will be detailed, as a non-limitative example.
- Such preferred method consists in providing a semi-finished casting of steel with a chemical composition of the prime steel according to the invention.
- the casting can be done either into ingots or continuously in form of thin slabs or thin strips, i.e. with a thickness ranging from approximately 220 mm for slabs up to several tens of millimeters for thin strip.
- a slab having the chemical composition according to the invention is manufactured by continuous casting wherein the slab optionally underwent a direct soft reduction during the continuous casting process to avoid central segregation and to ensure a ratio of local Carbon to nominal Carbon kept below 1.10.
- the slab provided by continuous casting process can be used directly at a high temperature after the continuous casting or may be first cooled to room temperature and then reheated for hot rolling.
- the temperature of the slab which is subjected to hot rolling, must be at least 1000° C. and must be below 1280° C. In case the temperature of the slab is lower than 1280° C., excessive load is imposed on a rolling mill and, further, the temperature of the steel may decrease to a Ferrite transformation temperature during finishing rolling, whereby the steel will be rolled in a state in which transformed Ferrite is contained in the structure. Therefore, the temperature of the slab must be high enough so that hot rolling should be completed in the temperature range of Ac3 to Ac3+100° C. Reheating at temperatures above 1280° C. must be avoided because they are industrially expensive.
- the sheet obtained in this manner is then cooled at a cooling rate of at least 20° C./s to the coiling temperature which must be below 650° C.
- the cooling rate will be less than or equal to 200° C./s.
- the hot rolled steel sheet is then coiled at a coiling temperature below 650° C. to avoid ovalization and preferably between 475° C. and 625° C. to avoid scale formation, with an even preferred range for such coiling temperature between 500° C. and 625° C.
- the coiled hot rolled steel sheet is then cooled down to room temperature before subjecting it to optional hot band annealing.
- the hot rolled steel sheet may be subjected to an optional scale removal step to remove the scale formed during the hot rolling before optional hot band annealing.
- the hot rolled sheet may then have subjected to an optional hot band annealing.
- such hot band annealing is performed at temperatures between 400° C. and 750° C., preferably for at least 12 hours and not more than 96 hours, the temperature preferably remaining below 750° C. to avoid transforming partially the hot-rolled microstructure and, therefore, possibly losing the microstructure homogeneity.
- an optional scale removal step of this hot rolled steel sheet may be performed through, for example, pickling of such sheet.
- This hot rolled steel sheet is then subjected to cold rolling to obtain a cold rolled steel sheet with a thickness reduction between 35 to 90%.
- the cold rolled steel sheet is heated at a heating rate which is of at least 2° C./s and preferably greater than 3° C./s, to a soaking temperature Tsoak between Ac3 and Ac3+100° C. and preferably between Ac3+10° C. and Ac3+100° C., wherein Ac3 for the steel sheet is calculated by using the following formula:
- the cold rolled steel sheet is held at Tsoak during 10 seconds to 500 seconds to ensure a complete recrystallization and full transformation to austenite of the strongly work hardened initial structure.
- the cold rolled steel sheet is then cooled in a two steps cooling process wherein the first step of cooling starts from Tsoak, the cold rolled steel sheet being cooled down, at a cooling rate CR1 between 15° C./s and 150° C./s, to a temperature T1 which is in a range between 650° C. and 750° C.
- the cooling rate CR1 for such first step of cooling is between 20° C./s and 120° C./s.
- the preferred T1 temperature for such first step is between 660° C. and 725° C.
- the cold rolled steel sheet is cooled down from T1 to a temperature T2 which is between Ms ⁇ 10° C. and 20° C., at a cooling rate CR2 of at least 50° C./s.
- the cooling rate CR2 for the second step of cooling is at least 100° C./s and more preferably at least 150° C./s.
- the preferred T2 temperature for such second step is between Ms ⁇ 50° C. and 20° C.
- Ms for the steel sheet is calculated by using the following formula:
- the cold rolled steel sheet is reheated to a tempering temperature Ttemper between 150° C. and 300° C. with a heating rate of at least 1° C./s and preferably of at least 2° C./s and more of at least 10° C./s during 100 s and 600 s.
- the preferred temperature range for tempering is between 200° C. and 300° C. and the preferred duration for holding at Ttemper is between 200 s and 500 s.
- the cold rolled steel sheet is cooled down to room temperature to obtain a cold rolled martensitic steel.
- the cold rolled martensitic steel sheet of the present invention may optionally be coated with zinc or zinc alloys, or with aluminum or aluminum alloys to improve its corrosion resistance.
- Table 1 Steel sheets made of steels with different compositions are gathered in Table 1, where the steel sheets are produced according to process parameters as stipulated in Table 2, respectively. Thereafter Table 3 gathers the microstructures of the steel sheets obtained during the trials and table 4 gathers the result of evaluations of obtained properties.
- Table 2 gathers the hot rolling and annealing process parameters implemented on cold rolled steel sheets to impart the steels of table 1 with requisite mechanical properties to become a cold rolled martensitic steel.
- the table 2 is as follows:
- Table 3 exemplifies the results of the tests conducted in accordance with the standards on different microscopes such as Scanning Electron Microscope for determining the microstructures of both the inventive and reference steels in terms of area fraction. The results are stipulated herein:
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PCT/IB2020/052999 WO2020229898A1 (en) | 2019-05-15 | 2020-03-30 | A cold rolled martensitic steel and a method of martensitic steel thereof |
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WO2024105428A1 (en) * | 2022-11-14 | 2024-05-23 | Arcelormittal | High toughness press-hardened steel part and method of manufacturing the same |
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KR20100034118A (ko) | 2008-09-23 | 2010-04-01 | 포항공과대학교 산학협력단 | 마르텐사이트 조직을 가진 초고강도 용융아연도금 강판 및 그 제조 방법 |
JP5136609B2 (ja) * | 2010-07-29 | 2013-02-06 | Jfeスチール株式会社 | 成形性および耐衝撃性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
WO2013065346A1 (ja) * | 2011-11-01 | 2013-05-10 | Jfeスチール株式会社 | 曲げ特性と低温靭性に優れた高強度熱延鋼板およびその製造方法 |
JP5821912B2 (ja) * | 2013-08-09 | 2015-11-24 | Jfeスチール株式会社 | 高強度冷延鋼板およびその製造方法 |
WO2015088523A1 (en) * | 2013-12-11 | 2015-06-18 | ArcelorMittal Investigación y Desarrollo, S.L. | Cold rolled and annealed steel sheet |
KR101568549B1 (ko) * | 2013-12-25 | 2015-11-11 | 주식회사 포스코 | 우수한 굽힘성 및 초고강도를 갖는 열간 프레스 성형품용 강판, 이를 이용한 열간 프레스 성형품 및 이들의 제조방법 |
CN113416892A (zh) * | 2014-02-05 | 2021-09-21 | 安赛乐米塔尔股份公司 | 可热成形的、可空气淬硬的、可焊的钢板 |
JP5896085B1 (ja) * | 2014-03-31 | 2016-03-30 | Jfeスチール株式会社 | 材質均一性に優れた高強度冷延鋼板およびその製造方法 |
WO2015177582A1 (fr) * | 2014-05-20 | 2015-11-26 | Arcelormittal Investigación Y Desarrollo Sl | Tôle d'acier doublement recuite à hautes caractéristiques mécaniques de résistance et ductilité, procédé de fabrication et utilisation de telles tôles |
WO2017006144A1 (en) * | 2015-07-09 | 2017-01-12 | Arcelormittal | Steel for press hardening and press hardened part manufactured from such steel |
KR101725274B1 (ko) | 2015-10-16 | 2017-04-10 | 삼화스틸(주) | 고강도 강판 및 그 제조방법 |
KR101767780B1 (ko) * | 2015-12-23 | 2017-08-24 | 주식회사 포스코 | 고항복비형 고강도 냉연강판 및 그 제조방법 |
WO2017125773A1 (en) * | 2016-01-18 | 2017-07-27 | Arcelormittal | High strength steel sheet having excellent formability and a method of manufacturing the same |
CN107619993B (zh) * | 2016-07-13 | 2019-12-17 | 上海梅山钢铁股份有限公司 | 屈服强度750MPa级冷轧马氏体钢板及其制造方法 |
MX2019001828A (es) * | 2016-08-30 | 2019-06-06 | Jfe Steel Corp | Lamina de acero y metodo para la fabricacion de la misma. |
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WO2024105429A1 (en) * | 2022-11-14 | 2024-05-23 | Arcelormittal | High toughness press-hardened steel part and method of manufacturing the same |
WO2024105428A1 (en) * | 2022-11-14 | 2024-05-23 | Arcelormittal | High toughness press-hardened steel part and method of manufacturing the same |
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WO2020229877A1 (en) | 2020-11-19 |
MA55949A (fr) | 2022-03-23 |
CA3140117C (en) | 2024-01-02 |
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JP2024045307A (ja) | 2024-04-02 |
ZA202107698B (en) | 2022-06-29 |
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CN113748219B (zh) | 2023-06-20 |
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