TWI591188B - High-strength steel material and method for manufacturing the same - Google Patents
High-strength steel material and method for manufacturing the same Download PDFInfo
- Publication number
- TWI591188B TWI591188B TW102118540A TW102118540A TWI591188B TW I591188 B TWI591188 B TW I591188B TW 102118540 A TW102118540 A TW 102118540A TW 102118540 A TW102118540 A TW 102118540A TW I591188 B TWI591188 B TW I591188B
- Authority
- TW
- Taiwan
- Prior art keywords
- content
- steel
- strength
- weight
- strength steel
- Prior art date
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
Description
本發明是有關於一種鋼材,且特別是有關於一種高強度鋼材(HSS)及其製造方法。 This invention relates to a steel material, and more particularly to a high strength steel (HSS) and method of making same.
傳統之高強度鋼材的抗拉強度(Tensile Strength;TS)為300 MPa至700 MPa。高強度鋼材的深衝性及延伸率(Elongation;EL)常隨其強度的增加而下降。舉例而言,高強度鋼材之抗拉強度從370MPa等級增加至590MPa等級時,鋼材之延伸率從34%大幅下降至20%。而且,值得注意的是,高強度鋼材之抗拉強度大於400MPa時,鋼材之延伸率即低於30%。這樣意味著,高強度鋼材之強度上升時,其成形性下降,如此將導致鋼材在成形過程中產生破裂的問題。 The traditional high-strength steel has a Tensile Strength (TS) of 300 MPa to 700 MPa. The deep drawability and elongation (Elongation; EL) of high-strength steels often decrease with increasing strength. For example, when the tensile strength of high-strength steel is increased from 370 MPa to 590 MPa, the elongation of steel is greatly reduced from 34% to 20%. Moreover, it is worth noting that when the tensile strength of high-strength steel is greater than 400 MPa, the elongation of the steel is less than 30%. This means that when the strength of the high-strength steel is increased, the formability is lowered, which causes a problem that the steel material is cracked during the forming process.
以美國汽車工程師學會(SAE)之J2340規範為例,取抗拉強度大於490MPa的鋼材,例如420X鋼材。此鋼材係利用鈮、鈦、釩、碳與氮形成析出強化,藉此達成鋼材強化而獲得所需強度。以此SAE J2340 420X鋼材之機械性質為抗拉強度大於490MPa,降伏強度(Yield Strength;YS)大於420MPa,延伸率大於18%。由此可知,雖然此鋼 材之強度大,但延伸率低,故不利於成形加工。 Take the J2340 specification of the Society of Automotive Engineers (SAE) as an example, taking steel with a tensile strength greater than 490 MPa, such as 420X steel. This steel material is formed by precipitation strengthening using niobium, titanium, vanadium, carbon and nitrogen, thereby achieving steel reinforcement to obtain the required strength. The mechanical properties of the SAE J2340 420X steel are greater than 490 MPa, the yield strength (YS) is greater than 420 MPa, and the elongation is greater than 18%. It can be seen that although this steel The strength of the material is large, but the elongation is low, which is not conducive to the forming process.
因此,本發明之一態樣就是在提供一種高強度鋼材及其製造方法,其係藉由調整鋼胚之組成及/或各階段製程控制,可在提高鋼材之強度下,兼顧鋼材之延展性與成形性。 Therefore, one aspect of the present invention is to provide a high-strength steel material and a method for manufacturing the same, which can improve the strength of the steel and the ductility of the steel by adjusting the composition of the steel preform and/or the process control at each stage. And formability.
本發明之另一態樣就是在提供一種高強度鋼材及其製造方法,其利用封盒式退火(BA)技術對完軋鋼材進行退火,因此可產製出具有較大厚度的鋼板。 Another aspect of the present invention provides a high-strength steel material and a method of manufacturing the same, which utilizes a box-type annealing (BA) technique to anneal a finished steel material, thereby producing a steel sheet having a large thickness.
根據本發明之上述目的,提出一種高強度鋼材。此高強度鋼材包含含量0.05wt%至0.22wt%的碳、含量0.05wt%至1.50wt%的錳、含量0.07wt%至0.12wt%的磷、含量小於0.02wt%的硫、含量小於0.04wt%的矽、含量0.025wt%至0.100wt%的鋁、含量0.002wt%至0.009wt%的氮、含量小於0.004wt%的鈦以及具有剩餘含量之鐵。 According to the above object of the present invention, a high strength steel material is proposed. The high-strength steel material comprises carbon in an amount of 0.05 wt% to 0.22 wt%, manganese in an amount of 0.05 wt% to 1.50 wt%, phosphorus in a content of 0.07 wt% to 0.12 wt%, sulfur in an amount of less than 0.02 wt%, and a content of less than 0.04 wt. % 矽, content 0.025 wt% to 0.100 wt% aluminum, 0.002 wt% to 0.009 wt% nitrogen, less than 0.004 wt% titanium, and iron having the remaining content.
依據本發明之一實施例,上述之鋁的含量0.025wt%至0.040wt%。 According to an embodiment of the invention, the aluminum content is from 0.025 wt% to 0.040 wt%.
依據本發明之另一實施例,上述之氮的含量0.004wt%至0.006wt%。 According to another embodiment of the present invention, the nitrogen content is from 0.004% by weight to 0.006% by weight.
根據本發明之上述目的,另提出一種高強度鋼材之製造方法,包含下列步驟。提供一鋼胚。其中,此鋼胚包含含量0.05wt%至0.22wt%的碳、含量0.05wt%至1.50wt%的錳、含量0.07wt%至0.12wt%的磷、含量小於0.02wt%的硫、含量小於0.04wt%的矽、含量0.025wt%至0.100wt%的 鋁、含量0.002wt%至0.009wt%的氮、含量小於0.004wt%的鈦、以及具有剩餘含量之鐵。對鋼胚進行一熱軋製程。對經熱軋製程後之鋼胚進行一冷軋製程,以獲得一完軋鋼材。對此完軋鋼材進行一封盒式退火製程。 According to the above object of the present invention, a method for producing a high-strength steel material is provided, which comprises the following steps. Provide a steel embryo. Wherein, the steel embryo comprises carbon with a content of 0.05 wt% to 0.22 wt%, manganese with a content of 0.05 wt% to 1.50 wt%, phosphorus with a content of 0.07 wt% to 0.12 wt%, sulfur having a content of less than 0.02 wt%, and a content of less than 0.04. Wt% of 矽, content of 0.025wt% to 0.100wt% Aluminium, a content of 0.002% by weight to 0.009% by weight of nitrogen, a content of less than 0.004% by weight of titanium, and iron having a residual content. A hot rolling process is carried out on the steel blank. A cold rolling process is performed on the steel blank after the hot rolling process to obtain a finished steel. A box annealing process is performed on the finished steel.
依據本發明之一實施例,上述進行熱軋製程時包含將一完軋溫度控制在大於或等於850℃。 According to an embodiment of the present invention, the performing the hot rolling process comprises controlling a finishing temperature to be greater than or equal to 850 °C.
依據本發明之另一實施例,上述進行冷軋製程時包含將一冷軋裁減率控制在35%至70%。 According to another embodiment of the present invention, the cold rolling process described above comprises controlling a cold rolling reduction rate of from 35% to 70%.
依據本發明之又一實施例,上述進行封盒式退火製程時包含:將一製程溫度控制在650℃至730℃、以及將一製程時間控制在8小時至15小時。 According to still another embodiment of the present invention, the performing the box annealing process comprises: controlling a process temperature between 650 ° C and 730 ° C, and controlling a process time from 8 hours to 15 hours.
依據本發明之再一實施例,上述高強度鋼材之製造方法更包含根據高強度鋼材之一預設抗拉強度且利用一預測公式,來調整鋼胚之成分、冷軋製程之一冷軋裁減率及/或封盒式退火製程之一製程溫度。其中,此預測公式為:預設抗拉強度=鋼胚之強度+0.0032×(錳之含量的ppm值)+0.0678×(磷之含量的ppm值)+0.5×(冷軋裁減率-49%)+0.33×(710℃-製程溫度)+0.066×(碳之含量的ppm值)。 According to still another embodiment of the present invention, the method for manufacturing the high-strength steel material further comprises: adjusting the tensile strength according to one of the high-strength steel materials and using a prediction formula to adjust the composition of the steel embryo, and one of the cold rolling reductions. Rate and / or one of the process temperatures of the box annealing process. Among them, the prediction formula is: preset tensile strength = strength of steel embryo + 0.0032 × (ppm value of manganese content) + 0.0678 × (ppm value of phosphorus content) + 0.5 × (cold rolling reduction rate - 49% ) +0.33 × (710 ° C - process temperature) + 0.066 × (ppm value of carbon content).
依據本發明之再一實施例,上述之鋁的含量0.025wt%至0.040wt%。 According to still another embodiment of the present invention, the aluminum content is from 0.025 wt% to 0.040 wt%.
依據本發明之再一實施例,上述之氮的含量0.004wr%至0.006wt%。 According to still another embodiment of the present invention, the nitrogen content is 0.004 wr% to 0.006 wt%.
100‧‧‧方法 100‧‧‧ method
102‧‧‧步驟 102‧‧‧Steps
104‧‧‧步驟 104‧‧‧Steps
106‧‧‧步驟 106‧‧‧Steps
108‧‧‧步驟 108‧‧‧Steps
為讓本發明之上述和其他目的、特徵、優點與實施例能更明顯易懂,所附圖式之說明如下: 第1圖係繪示依照本發明之一實施方式的一種高強度鋼材之製作流程圖。 The above and other objects, features, advantages and embodiments of the present invention will become more apparent and understood. 1 is a flow chart showing the manufacture of a high-strength steel according to an embodiment of the present invention.
第2圖係繪示依照本發明之一實施方式的高強度鋼材與美國鋼鐵協會(AISI)之微合金鋼材和一般連續退火之鋼材的抗拉強度與延伸率之關係圖。 2 is a graph showing the tensile strength and elongation of a high-strength steel according to an embodiment of the present invention, a microalloyed steel of the American Iron and Steel Institute (AISI), and a generally continuously annealed steel.
有鑑於傳統高強度鋼材在強度、以及延伸率與深衝性上無法有效兼顧,因此本發明在此提出一種藉由調整鋼材之組成及/或各階段製程的方式,來達成提高鋼材強度,並兼顧延展性及成形性。 In view of the fact that conventional high-strength steels cannot be effectively combined in strength, elongation and deep drawability, the present invention proposes an increase in steel strength by adjusting the composition of the steel and/or the process of each stage. Both ductility and formability.
在本發明之一實施方式中,高強度鋼材之機械性質可包含抗拉強度為300MPa至600 MPa,降伏強度為200MPa至400MPa,延伸率為30%至40%。此高強度鋼材可運用於需高強度且大量變形的部件,例如汽車前後保險桿、葉子板、引擎蓋、車門等等。除了可提供成品足夠強度,以增進安全性外,更可在製造時提供良好的成形性,有利於降低製作成本與提高製程良率。 In an embodiment of the present invention, the mechanical properties of the high strength steel may include a tensile strength of 300 MPa to 600 MPa, a relief strength of 200 MPa to 400 MPa, and an elongation of 30% to 40%. This high-strength steel can be used for parts that require high strength and large deformation, such as front and rear bumpers, fenders, hoods, doors, etc. In addition to providing sufficient strength of the finished product to enhance safety, it can provide good formability during manufacturing, which is beneficial to reduce production costs and improve process yield.
在一實施例中,此高強度鋼材之成分可例如包含有含量0.05wt%至0.22wt%的碳、含量0.05wt%至1.50wt%的錳、含量0.07wt%至0.12wt%的磷、含量小於0.02wt%的硫、含量小於0.04wt%的矽、含量0.025wt%至0.100wt%的鋁、含量0.002wt%至0.009wt%的氮、含量小於0.004wt%的鈦 以及具有剩餘含量之鐵。在一較佳實施例中,鋁之含量可例如為0.025wt%至0.040wt%。此外,氮之含量可例如為0.004wt%至0.006wt%。 In one embodiment, the composition of the high-strength steel may include, for example, a content of 0.05% by weight to 0.22% by weight of carbon, a content of 0.05% by weight to 1.50% by weight of manganese, and a content of 0.07% by weight to 0.12% by weight of phosphorus. Less than 0.02% by weight of sulfur, less than 0.04% by weight of cerium, 0.025% by weight to 0.100% by weight of aluminum, 0.002% by weight to 0.009% by weight of nitrogen, and less than 0.004% by weight of titanium And iron with the remaining content. In a preferred embodiment, the aluminum content may be, for example, from 0.025 wt% to 0.040 wt%. Further, the content of nitrogen may be, for example, 0.004% by weight to 0.006% by weight.
在一實施方式中,製作高強度鋼材時,可運用集合組織(Texture)控制、固溶強化、晶粒細化強化、以及球形化雪明碳鐵散佈強化等技術,在提升鋼材之強度下,兼顧鋼材之延伸率及深衝性。請參照第1圖,其係繪示依照本發明之一實施方式的一種高強度鋼材之製作流程圖。製作此高強度鋼材時,可先如方法100之步驟102般,先提供鋼胚。在一實施例中,此鋼胚之成分可包含有含量0.05wt%至0.22wt%的碳、含量0.05wt%至1.50wt%的錳、含量0.07wt%至0.12wt%的磷、含量小於0.02wt%的硫、含量小於0.04wt%的矽、含量0.025wt%至0.100wt%的鋁、含量0.002wt%至0.009wt%的氮、含量小於0.004wt%的鈦以及具有剩餘含量之鐵。在一較佳實施例中,鋁之含量可例如為0.025wt%至0.040wt%。此外,氮之含量可例如為0.004wt%至0.006wt%。此提供鋼胚之步驟102可以此鋼胚為原料進行煉鋼製程。 In one embodiment, when a high-strength steel material is produced, techniques such as texture control, solid solution strengthening, grain refinement strengthening, and spheroidized ferritic carbon iron dispersion strengthening can be used to enhance the strength of the steel. Take into account the elongation and deep drawability of steel. Please refer to FIG. 1 , which is a flow chart showing the manufacture of a high-strength steel according to an embodiment of the present invention. When making this high strength steel, the steel blank can be provided first as in step 102 of method 100. In an embodiment, the composition of the steel preform may comprise a content of 0.05% by weight to 0.22% by weight of carbon, a content of 0.05% by weight to 1.50% by weight of manganese, a content of 0.07% by weight to 0.12% by weight of phosphorus, and a content of less than 0.02. The wt% sulfur, the content of less than 0.04 wt% of antimony, the content of 0.025 wt% to 0.100 wt% of aluminum, the content of 0.002 wt% to 0.009 wt% of nitrogen, the content of less than 0.004 wt% of titanium and the balance of iron. In a preferred embodiment, the aluminum content may be, for example, from 0.025 wt% to 0.040 wt%. Further, the content of nitrogen may be, for example, 0.004% by weight to 0.006% by weight. The step 102 of providing the steel blank can use the steel blank as a raw material for the steel making process.
接著,如步驟104所述,對鋼胚進行熱軋製程。在一實施例中,對鋼胚進行熱軋製程時,可將完軋溫度控制在例如大於或等於850℃。接下來,可如步驟106所述,對鋼胚進行熱軋製程後,對此經熱軋後之鋼胚進行冷軋製程,以獲得完軋鋼材。在一實施例中,進行鋼胚之冷軋製程時,可將冷軋製程之冷軋裁減率控制在例如35%至70%。 Next, as described in step 104, the steel blank is subjected to a hot rolling pass. In one embodiment, the rolling temperature can be controlled, for example, to greater than or equal to 850 ° C when the steel blank is subjected to a hot rolling pass. Next, after the hot rolling process of the steel blank is performed as described in step 106, the hot rolled steel blank is subjected to a cold rolling process to obtain a rolled steel. In an embodiment, the cold rolling reduction of the cold rolling pass may be controlled to, for example, 35% to 70% when the cold rolling of the steel blank is performed.
形成完軋鋼材後,可如步驟108所述,對此完軋鋼材進行封盒式退火製程,而獲得所需之高強度鋼材。在其他實施例中,可根據產品需求,而在封盒式退火製程期間,鋼材進行進一步的調質與精整處理。在一示範實施例中,對完軋鋼材進行封盒式退火製程時,可將製程溫度控制在例如650℃至730℃,且可將製程時間控制在例如8小時至15小時。由於此實施方式採用封盒式退火製程,因此可產製厚度為2.0mm至3.2mm的較厚鋼材。 After the rolled steel material is formed, the finished steel can be subjected to a box annealing process as described in step 108 to obtain a desired high strength steel material. In other embodiments, the steel may be further tempered and finished during the encapsulation annealing process depending on the product requirements. In an exemplary embodiment, the process temperature may be controlled to, for example, 650 ° C to 730 ° C when the finished steel is subjected to a box annealing process, and the process time may be controlled, for example, from 8 hours to 15 hours. Since this embodiment adopts a box-type annealing process, a thick steel material having a thickness of 2.0 mm to 3.2 mm can be produced.
藉由應用此實施方式之鋼胚組成與製程建議,可控制鋼胚經熱軋製程、冷軋製程與封盒式退火製程後的集合組織,可獲得兼具延伸率、深衝性與高強度的鋼材。 By applying the steel preform composition and process proposal of this embodiment, the assembly of the steel embryo after the hot rolling, cold rolling and sealing annealing processes can be controlled, and the elongation, deep drawing and high strength can be obtained. Steel.
在一實施例中,針對高強度鋼材之製程參數中的熱軋完軋溫度、冷軋裁減率與封盒式退火之製程溫度進行實驗分析。另外,本實施例再針對鋼胚的化學組成、及鋼材之製程參數與所獲得之鋼材的抗拉強度推導出冶金之預測公式,如下列公式(1):預設抗拉強度=鋼胚之強度+0.0032×(鋼胚之錳含量的ppm值)+0.0678×(鋼胚之磷含量的ppm值)+0.5×(冷軋裁減率-49%)+0.33×(710℃-熱軋製程溫度)+0.066×(鋼胚之碳含量的ppm值) (公式1) In one embodiment, an experimental analysis is performed on the hot rolling finish temperature, the cold rolling reduction rate, and the process temperature of the box annealing in the process parameters of the high strength steel. In addition, in this embodiment, the metallurgical prediction formula is derived for the chemical composition of the steel preform, the process parameters of the steel, and the tensile strength of the obtained steel, such as the following formula (1): preset tensile strength = steel embryo Strength +0.0032×(ppm value of manganese content of steel embryo)+0.0678×(ppm value of phosphorus content of steel embryo)+0.5×(cold rolling reduction rate-49%)+0.33×(710°C-hot rolling range temperature ) +0.066 × (ppm value of carbon content of steel embryo) (Equation 1)
因此,可根據高強度鋼材之預設抗拉強度,而利用上述預測公式,來調整鋼胚之成分、冷軋製程之冷軋裁減率、及/或封盒式退火製程之製程溫度等。此外,更可利用金相與穿透式電子顯微鏡,來對熱軋、冷軋與封盒式退火 製程階段之顯微組織及集合組織進行詳細的分析,以了解高強度兼具高深衝性的冶金機制。 Therefore, according to the preset tensile strength of the high-strength steel, the above prediction formula can be used to adjust the composition of the steel blank, the cold rolling reduction rate of the cold rolling process, and/or the process temperature of the sealed annealing process. In addition, metallographic and transmission electron microscopy can be used for hot rolling, cold rolling and box annealing. Detailed analysis of the microstructure and aggregate structure of the process stage to understand the metallurgical mechanism of high strength and high deep drawability.
以下利用多個實施例,來更具體說明利用本實施方式的技術內容與功效。下表一列出以上述冶金預測公式預測與實驗在這些實施例之鋼胚成分與製程條件下所獲得之鋼材的機械性質。在這些實施例中,鋼胚中其餘的矽、硫、鋁、氮與鈦等微量元素如上述實施例所述之範圍。 The technical contents and effects of the present embodiment will be more specifically described below using a plurality of embodiments. Table 1 below lists the mechanical properties of the steels obtained under the above-mentioned metallurgical prediction formulas and experimentally obtained under the steel embryo components and process conditions of these examples. In these examples, the remaining trace elements such as barium, sulfur, aluminum, nitrogen and titanium in the steel embryo are as described in the above examples.
由上表一可知,抗拉強度大於400 Mpa的高強度鋼材的延伸率均大於30%。因此,本實施方式提出藉由化學組成與製程參數的配合調整,可獲得高強度且兼顧延伸率的鋼材。這樣的高強度鋼材具有良好成形性,有利於後續成形加工的進行。 It can be seen from the above Table 1 that the elongation of high-strength steel with tensile strength greater than 400 Mpa is greater than 30%. Therefore, in the present embodiment, it is proposed that a steel material having high strength and an elongation ratio can be obtained by adjusting the chemical composition and the process parameters. Such high-strength steel has good formability and is advantageous for subsequent forming processing.
請參照第2圖,其係繪示依照本發明之一實施方式的高強度鋼材與美國鋼鐵協會之微合金鋼材和一般連續退火之鋼材的抗拉強度與延伸率之關係圖。從第2圖可看出,隨著抗拉強度的增加,美國鋼鐵協會之微合金鋼材、與一般連續退火處理之鋼材的延伸率均快速下降。另一方面, 隨著抗拉強度的增加,本發明之實施例中厚度大於2mm之經封盒式退火製程後的鋼材與經封盒式退火製程後之鋼材目標之延伸率的下降明顯較為緩和。 Please refer to FIG. 2, which is a graph showing the relationship between tensile strength and elongation of a high-strength steel according to an embodiment of the present invention, a microalloyed steel of the American Iron and Steel Association, and a steel which is generally continuously annealed. As can be seen from Fig. 2, as the tensile strength increases, the elongation of the micro-alloyed steel of the American Iron and Steel Association and the steel which is generally continuously annealed rapidly decreases rapidly. on the other hand, As the tensile strength increases, the decrease in the elongation of the steel after the sealed annealing process and the steel after the sealed annealing process in the embodiment of the present invention is significantly more moderate.
由上述之實施方式可知,本發明之一優點為藉由調整鋼胚之組成及/或各階段製程控制,可在提高鋼材之強度下,兼顧鋼材之延展性與成形性。 As can be seen from the above embodiments, one of the advantages of the present invention is that by adjusting the composition of the steel preform and/or the process control at each stage, the ductility and formability of the steel can be achieved while increasing the strength of the steel.
由上述之實施方式可知,本發明之另一優點就是因為本發明利用封盒式退火技術對完軋鋼材進行退火,因此可產製出具有較大厚度的鋼板。 As can be seen from the above embodiments, another advantage of the present invention is that since the present invention utilizes a box-type annealing technique to anneal a finished steel material, a steel sheet having a large thickness can be produced.
雖然本發明已以實施例揭露如上,然其並非用以限定本發明,任何在此技術領域中具有通常知識者,在不脫離本發明之精神和範圍內,當可作各種之更動與潤飾,因此本發明之保護範圍當視後附之申請專利範圍所界定者為準。 While the present invention has been described above by way of example, it is not intended to be construed as a limitation of the scope of the invention. Therefore, the scope of the invention is defined by the scope of the appended claims.
100‧‧‧方法 100‧‧‧ method
102‧‧‧步驟 102‧‧‧Steps
104‧‧‧步驟 104‧‧‧Steps
106‧‧‧步驟 106‧‧‧Steps
108‧‧‧步驟 108‧‧‧Steps
Claims (10)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
TW102118540A TWI591188B (en) | 2013-05-24 | 2013-05-24 | High-strength steel material and method for manufacturing the same |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
TW102118540A TWI591188B (en) | 2013-05-24 | 2013-05-24 | High-strength steel material and method for manufacturing the same |
Publications (2)
Publication Number | Publication Date |
---|---|
TW201444983A TW201444983A (en) | 2014-12-01 |
TWI591188B true TWI591188B (en) | 2017-07-11 |
Family
ID=52706926
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
TW102118540A TWI591188B (en) | 2013-05-24 | 2013-05-24 | High-strength steel material and method for manufacturing the same |
Country Status (1)
Country | Link |
---|---|
TW (1) | TWI591188B (en) |
-
2013
- 2013-05-24 TW TW102118540A patent/TWI591188B/en active
Also Published As
Publication number | Publication date |
---|---|
TW201444983A (en) | 2014-12-01 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP7321828B2 (en) | High-strength 6xxx aluminum alloy and method for making same | |
WO2013147228A1 (en) | Manufacturing method for hot press-molded steel member, and hot press-molded steel member | |
WO2011126154A1 (en) | High-strength steel sheet having excellent hot rolling workability, and process for production thereof | |
CN104593674A (en) | Hot-dip galvanized ultra-low carbon bake-hardening steel and production method thereof | |
EP3234208B1 (en) | Aluminum alloy suitable for the high speed production of aluminum bottle and the process of manufacturing thereof | |
US11788178B2 (en) | Methods of making highly-formable aluminum alloys and aluminum alloy products thereof | |
CN103602884A (en) | Ultralow-carbon aluminum-killed steel plate and production method thereof | |
CN104532123B (en) | A kind of preparation method of hot-dip galvanizing sheet steel | |
JP4833698B2 (en) | High strength steel plate for die quench | |
CN104726766A (en) | Low-cost 260 MPa-level steel for automobile and production method thereof | |
TWI504756B (en) | Manufacture method of high strength and high ductility steel | |
EP3733889A1 (en) | Magnesium alloy sheet and method for producing same | |
TWI591188B (en) | High-strength steel material and method for manufacturing the same | |
KR20100009683A (en) | Heat treatment method for al alloy panel | |
CN105088063B (en) | Work-hardening high-strength steel and manufacturing method thereof | |
CN105734407A (en) | Novel ultra-thin microalloy high-strength steel and preparation method thereof | |
KR101481909B1 (en) | Manufacturing method of magnesium alloy | |
TWI531661B (en) | Bake hardenable steel and method for manufacturing the same | |
JP2008246508A (en) | Bending method of aluminum alloy material | |
KR101612180B1 (en) | Manufacturing method of low manganese twip steel | |
CN112795837B (en) | 1300Mpa high-toughness cold-formed steel plate and production method thereof | |
TWI711706B (en) | Automobile steel material with high yield strength and method of manufacturing the same | |
CN104372243B (en) | 440MPa grade cold rolled strip steel and production method thereof | |
CN105378128B (en) | Processability and the excellent hot rolled steel plate of aging resistance and its manufacture method | |
KR101572318B1 (en) | Method of manufacturing steel product |