TWI564402B - High strength steel exhibiting good ductility and method of production via quenching and partitioning treatment by zinc bath - Google Patents

High strength steel exhibiting good ductility and method of production via quenching and partitioning treatment by zinc bath Download PDF

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TWI564402B
TWI564402B TW103117430A TW103117430A TWI564402B TW I564402 B TWI564402 B TW I564402B TW 103117430 A TW103117430 A TW 103117430A TW 103117430 A TW103117430 A TW 103117430A TW I564402 B TWI564402 B TW I564402B
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temperature
steel sheet
austenite
cooling
less
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TW201502284A (en
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葛蘭特 艾倫 湯瑪斯
馬汀斯 路易斯Ｇ 葛薩
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Ａｋ鋼鐵資產公司
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
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    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
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    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Description

展現良好延展性之高強度鋼及藉由經鋅浴槽淬火及分配處理之製造方法 High-strength steel exhibiting good ductility and manufacturing method by quenching and distributing treatment through zinc bath

本申請案主張臨時專利申請案第61/824,643號之優先權，該臨時專利申請案標題為「展現良好延展性之高強度鋼及藉由熔融鋅浴槽的下游在線分配處理之製造方法」，申請於2013年5月17日。申請案第61/824,643號之揭示內容以引用的方式併入本文中。 The present application claims the priority of Provisional Patent Application No. 61/824,643, entitled "Production Method for High-Strength Steel Showing Good Ductility and Downstream Online Dispensing Treatment of Molten Zinc Bath", Application On May 17, 2013. The disclosure of the application Serial No. 61/824,643 is incorporated herein by reference.

需要製造具有高強度及良好成形性特徵之鋼。然而，由於諸如相對低含量合金化添加物之合意性及工業生產線之熱加工能力的侷限性的因素，展現該等特徵的鋼的商業製造一直為困難的。本發明係關於鋼組份及加工方法，該方法使用熱浸漬鍍鋅/鍍鋅退火(hot-dip galvanizing/galvannealing，HDG)製程以使得所得的鋼展現高強度及冷成形性。 There is a need to produce steels with high strength and good formability characteristics. However, commercial manufacture of steel exhibiting such characteristics has been difficult due to factors such as the desirability of relatively low levels of alloying additives and the limitations of the thermal processing capabilities of industrial lines. The present invention relates to a steel component and a processing method which uses a hot-dip galvanizing/galvannealing (HDG) process to render the resulting steel exhibit high strength and cold formability.

本發明之鋼係使用組份與經改良之HDG製程製造，兩者共同產生所得的通常由馬氏體(martensite)及奧氏體(austenite)(除了其他組份之外)組成的微結構。為達成此類微結構，組份包括某些合金化添加物且HDG製程包括某些製程改良，其全部至少部分地係關於驅使奧氏體轉化成馬氏體，之後在室溫下部分穩定奧氏體。 The steel-based components of the present invention are manufactured using a modified HDG process, which together produce a resulting microstructure generally consisting of martensite and austenite (other than the other components). To achieve such microstructures, the components include certain alloying additives and the HDG process includes certain process modifications, all at least in part to drive the transformation of austenite to martensite, and then partially stabilize at room temperature. Clan.

10‧‧‧熱浸漬鍍鋅或鍍鋅退火熱分佈 10‧‧‧Hot-dip galvanizing or galvanizing annealing heat distribution

12‧‧‧最高金屬溫度 12‧‧‧Highest metal temperature

14‧‧‧恆定溫度 14‧‧‧ Constant temperature

16‧‧‧鍍鋅退火溫度 16‧‧‧galvanizing annealing temperature

18‧‧‧淬火溫度 18‧‧‧Quenching temperature

20‧‧‧較高分配溫度 20‧‧‧Higher distribution temperature

22‧‧‧較低分配溫度 22‧‧‧lower distribution temperature

24‧‧‧替代分配溫度 24‧‧‧Alternative distribution temperature

40‧‧‧實線 40‧‧‧solid line

42‧‧‧最高金屬溫度 42‧‧‧Highest metal temperature

44‧‧‧淬火 44‧‧‧Quenching

46‧‧‧淬火溫度 46‧‧ ‧ quenching temperature

48‧‧‧再加熱 48‧‧‧Reheating

50‧‧‧鍍鋅浴槽溫度/分配溫度 50‧‧‧Zinc plating bath temperature/distribution temperature

52‧‧‧浴槽/分配溫度 52‧‧‧bath/distribution temperature

54‧‧‧冷卻 54‧‧‧cooling

併入且構成此說明書之一部分的隨附圖式說明實施例，且與上文提供的大體描述及下文提供的實施例之詳細描述一起，用以解釋本發明之原理。 The accompanying drawings, which are incorporated in FIG

圖1描繪HDG溫度分佈之示意圖，該HDG溫度分佈具有在鍍鋅/鍍鋅退火之後進行的分配步驟。 Figure 1 depicts a schematic of the HDG temperature profile with a dispensing step performed after galvanizing/galvanizing annealing.

圖2描繪HDG溫度分佈之示意圖，該HDG溫度分佈具有在鍍鋅/鍍鋅退火期間進行的分配步驟。 Figure 2 depicts a schematic of the HDG temperature profile with a dispensing step performed during galvanizing/galvanizing annealing.

圖3描繪一個實施例之相對於冷卻速率繪製的洛氏硬度(Rockwell hardness)之曲線。 Figure 3 depicts a plot of Rockwell hardness plotted against cooling rate for one embodiment.

圖4描繪另一實施例之相對於冷卻速率繪製的洛氏硬度之曲線。 Figure 4 depicts a plot of Rockwell hardness plotted against cooling rate for another embodiment.

圖5描繪另一實施例之相對於冷卻速率繪製的洛氏硬度之曲線。 Figure 5 depicts a plot of Rockwell hardness plotted against cooling rate for another embodiment.

圖6描繪圖3之實施例之六個顯微照相圖，該等顯微照相圖自以各種冷卻速率冷卻的樣品取得。 Figure 6 depicts six photomicrographs of the embodiment of Figure 3 taken from samples cooled at various cooling rates.

圖7描繪圖4之實施例之六個顯微照相圖，該等顯微照相圖自以各種冷卻速率冷卻的樣品取得。 Figure 7 depicts six photomicrographs of the embodiment of Figure 4 taken from samples cooled at various cooling rates.

圖8描繪圖5之實施例之六個顯微照相圖，該等顯微照相圖自以各種冷卻速率冷卻的樣品取得。 Figure 8 depicts six photomicrographs of the embodiment of Figure 5 taken from samples cooled at various cooling rates.

圖9描繪數個實施例之隨奧氏體化溫度(austenitization temperature)而變的拉伸數據之曲線。 Figure 9 depicts a plot of tensile data as a function of austenitization temperature for several embodiments.

圖10描繪數個實施例之隨奧氏體化溫度而變的拉伸數據之曲線。 Figure 10 depicts a plot of tensile data as a function of austenitizing temperature for several embodiments.

圖11描繪數個實施例之隨淬火溫度而變的拉伸數據之曲線。 Figure 11 depicts a plot of tensile data as a function of quenching temperature for several embodiments.

圖12描繪數個實施例之隨淬火溫度而變的拉伸數據之曲線。 Figure 12 depicts a plot of tensile data as a function of quenching temperature for several embodiments.

圖1顯示用於在具有某一化學組份(下文更詳細地描述)之鋼片中 達成高強度及冷成形性之熱循環的示意性圖示。詳言之，圖1顯示典型的熱浸漬鍍鋅或鍍鋅退火熱分佈(10)，其中製程改良用虛線顯示。在一個實施例中，製程通常包含奧氏體化，之後快速冷卻至特定淬火溫度以將奧氏體部分轉化為馬氏體，且保持在高溫、分配溫度下以使得碳自馬氏體中擴散出且進入剩餘的奧氏體，由此在室溫下穩定奧氏體。在一些實施例中，顯示於圖1中之熱分佈可與習知的連續熱浸漬鍍鋅或鍍鋅退火生產線一起使用，但此類生產線並非必需的。 Figure 1 shows for use in steel sheets with a certain chemical composition (described in more detail below) A schematic representation of a thermal cycle that achieves high strength and cold formability. In particular, Figure 1 shows a typical hot dip galvanizing or galvanizing annealing heat distribution (10) in which process improvements are shown in dashed lines. In one embodiment, the process typically includes austenitization followed by rapid cooling to a particular quenching temperature to convert the austenite portion to martensite and maintained at a high temperature, distribution temperature to diffuse carbon from the martensite. It exits and enters the remaining austenite, thereby stabilizing austenite at room temperature. In some embodiments, the heat profile shown in Figure 1 can be used with conventional continuous hot dip galvanizing or galvanizing annealing lines, but such lines are not required.

如可見，首先加熱鋼片至最高金屬溫度(12)。在所說明的實例中之最高金屬溫度(12)顯示為至少高於奧氏體轉化溫度(A1)(例如雙相奧氏體+肥粒鐵(ferrite)區域)。由此，在最高金屬溫度(12)下，鋼之至少一部分將轉化成奧氏體。儘管圖1顯示最高金屬溫度(12)為僅高於A1，應理解，在一些實施例中最高金屬溫度亦可包括高於肥粒鐵完全轉化成奧氏體之溫度(A3)(例如單相奧氏體區域)的溫度。 As can be seen, the steel sheet is first heated to the highest metal temperature (12). Peak metal temperature in the examples described in the (12) shows at least above the austenite transition temperature of (A 1) (e.g. ferrite + austenite dual phase (Ferrite) region). Thus, at the highest metal temperature (12), at least a portion of the steel will be converted to austenite. Although FIG. 1 shows the highest metal temperature (12) is just above the A 1, to be understood that in some embodiments may also include a peak metal temperature above the ferrite to austenite temperature complete conversion of (A 3) (e.g. The temperature of the single-phase austenite region).

隨後鋼片經受快速冷卻。隨著鋼片冷卻，一些實施例在冷卻中可包括短暫的中斷以用於鍍鋅或鍍鋅退火。在使用鍍鋅之實施例中，由於來自熔融鋅鍍鋅浴槽之熱量，鋼片可短暫維持恆定溫度(14)。又在其他實施例中，可使用鍍鋅退火製程且可稍微提高鋼片之溫度至可進行鍍鋅退火製程之鍍鋅退火溫度(16)。但是，在其他實施例中，可完全省去鍍鋅或鍍鋅退火製程且可連續冷卻鋼片。 The steel sheet is then subjected to rapid cooling. As the steel sheet cools, some embodiments may include a brief interruption in cooling for galvanizing or galvanizing annealing. In the embodiment using galvanizing, the steel sheet can be maintained at a constant temperature (14) for a short time due to heat from the molten zinc galvanizing bath. In still other embodiments, a galvannealing process can be used and the temperature of the steel sheet can be increased slightly to the galvanizing annealing temperature (16) where the galvanizing annealing process can be performed. However, in other embodiments, the galvanizing or galvanizing annealing process can be completely eliminated and the steel sheet can be continuously cooled.

顯示鋼片在低於鋼片之馬氏體起始溫度(Ms)時繼續快速冷卻至預定淬火溫度(18)。應理解，冷卻至Ms之冷卻速率可足夠高以使在最高金屬溫度(12)下形成的奧氏體之至少一部分轉化成馬氏體。換言之，冷卻速率可足夠快以使奧氏體轉化成馬氏體而非其他在相對較低冷卻速率下轉化的非馬氏體組份(諸如肥粒鐵、波來鐵(pearlite)或韌鋼(bainite))。 It is shown that the steel sheet continues to cool rapidly to a predetermined quenching temperature (18) below the martensite starting temperature (M s ) of the steel sheet. It should be understood, it cooled to a cooling rate of M s may be sufficiently high so as to form austenite at the highest metal temperature (12) at least a portion is converted into martensite. In other words, the cooling rate can be fast enough to convert austenite to martensite rather than other non-martensitic components (such as ferrite iron, pearlite or toughness steel) that are converted at relatively low cooling rates. (bainite)).

如顯示於圖1中，淬火溫度(18)低於Ms。淬火溫度(18)與Ms之間 的差值可視所用的鋼片之個別組份而變化。然而，在許多實施例中，在淬火溫度(18)與Ms之間的差值可足夠大以形成充足量之馬氏體從而在最終冷卻時充當碳源以穩定奧氏體且避免形成過量的「新製」馬氏體。另外，淬火溫度(18)可足夠高以避免在初始淬火期間消耗過多的奧氏體(例如對於給定實施例，避免奧氏體之過量的碳富集多於穩定奧氏體所需的碳富集)。 As shown in Figure 1, the quenching temperature (18) is lower than M s . Individual components vary between visual quenching temperature difference (18) with M s of the steel used. However, in many embodiments, the difference between the quenching temperature (18) and M s may be large enough to form a sufficient amount of martensite, act as carbon source in the final cooling to stabilize the austenite and avoid excessive "New" martensite. Additionally, the quenching temperature (18) can be sufficiently high to avoid consuming excessive austenite during initial quenching (e.g., for a given embodiment, avoiding excessive carbon enrichment of austenite more than carbon required to stabilize austenite) Enrichment).

在許多實施例中，淬火溫度(18)可自約191℃至約281℃變化，儘管並不需要該限制。另外，對於給定鋼組份可計算淬火溫度(18)。對於此類計算值，淬火溫度(18)對應於在分配之後具有室溫Ms溫度之殘留奧氏體。計算淬火溫度(18)之方法描述於J.G.Speer,A.M.Streicher,D.K.Matlock,F.Rizzo及G.Krauss,「Quenching And Partitioning：A Fundamentally New Process to Create High Strength Trip Sheet Microstructures」,Austenite Formation and Decomposition，第505至522頁，2003；及Proceedings of the International Conference on Advanced High Strength Sheet Steels for Automotive Applications,2004中之A.M.Streicher,J.G.J.Speer,D.K.Matlock及B.C.De Cooman,「Quenching and Partitioning Response of a Si-Added TRIP Sheet Steel」中，其主題以引用之方式併入本文中。 In many embodiments, the quenching temperature (18) can vary from about 191 °C to about 281 °C, although this limitation is not required. In addition, the quenching temperature (18) can be calculated for a given steel component. For such calculated values, the quenching temperature (18) corresponds to retained austenite having a room temperature M s temperature after dispensing. The method for calculating the quenching temperature (18) is described in JGSpeer, AMStreicher, DK Matlock, F. Rizzo and G. Krauss, "Quenching And Partitioning: A Fundamentally New Process to Create High Strength Trip Sheet Microstructures", Austenite Formation and Decomposition , Section 505 522 pages, 2003; and Proceedings of the International Conference on Advanced High Strength Sheet Steels for Automotive Applications , 2004, AMStreicher, JGJSpeer, DK Matlock and BC De Cooman, "Quenching and Partitioning Response of a Si-Added TRIP Sheet Steel" The subject matter is incorporated herein by reference.

淬火溫度(18)可足夠低(相對於Ms)以形成充足量之馬氏體從而在最終淬火時充當碳源以穩定奧氏體且避免形成過量的「新製」馬氏體。或者，淬火溫度(18)可足夠高以避免在初始淬火期間消耗過多奧氏體且形成如下情況，即殘留奧氏體之潛在的碳富集多於在室溫下穩定奧氏體所需的碳富集。在一些實施例中，適合之淬火溫度(18)可對應於在分配之後具有室溫Ms溫度之殘留奧氏體。Speer及Streicher等人(上文)擁有概念化計算，其提供探索可產生所需的微結構之製程選擇的準則。該等計算假定理想化的完全分配，且可藉由應用 Koistinen-Marburger(KM)關係式兩次(f m =1-e -1.1x10-2(△T))來進行，首先對初始淬火至淬火溫度(18)應用，且隨後對在室溫下最終淬火應用(如下文所進一步描述)。可使用基於奧氏體化學之經驗公式(諸如安德魯氏(Andrew's)線形表達式之經驗公式)來估算KM表達式中的Ms溫度：Ms(℃)=539-423C-30.4Mn-7.5Si+30Al Quenching temperature (18) may be low enough (relative to M s) to form a sufficient amount of martensite, it acts as a carbon source for the final hardening to stabilize the austenite and avoid excessive "fresh" martensite. Alternatively, the quenching temperature (18) may be sufficiently high to avoid excessive austenite consumption during the initial quenching and is formed by the potential carbon enrichment of retained austenite more than is required to stabilize austenite at room temperature. Carbon enrichment. In some embodiments, a suitable quenching temperature (18) may correspond to residual austenite having a room temperature M s temperature after dispensing. Speer and Streicher et al. (above) have conceptual calculations that provide guidelines for exploring process choices that can produce the desired microstructure. These calculations assume an idealized complete distribution and can be performed by applying the Koistinen-Marburger (KM) relationship twice ( f m = 1 - e - 1.1 x 10-2 (Δ T ) ), first to the initial quenching Application to quenching temperature (18) and subsequent final quenching at room temperature (as further described below). The empirical formula based on austenitic chemistry (such as the empirical formula of Andrew's linear expression) can be used to estimate the M s temperature in the KM expression: Ms ( °C ) = 539-423 C -30.4 Mn -7.5 Si +30 Al

由Speer等人概念化的計算結果可表明可產生最大量之殘留奧氏體之淬火溫度(18)。對於高於最高溫度之淬火溫度(18)，在初始淬火之後存在大量奧氏體部分；然而，沒有足夠的馬氏體來充當碳源以穩定此奧氏體。因此，對於較高淬火溫度，在最終淬火期間形成增加量之新製馬氏體。對於低於最高溫度之淬火溫度，在初始淬火期間可能消耗不令人滿意的量之奧氏體，且可能存在可能自馬氏體分配之過量的碳。 The calculations conceptualized by Speer et al. indicate the maximum quenching temperature (18) of retained austenite. For the quenching temperature (18) above the maximum temperature, a large amount of austenite portions are present after the initial quenching; however, there is not enough martensite to act as a carbon source to stabilize the austenite. Thus, for higher quenching temperatures, an increased amount of new martensite is formed during final quenching. For quenching temperatures below the maximum temperature, an unsatisfactory amount of austenite may be consumed during the initial quenching, and there may be an excess of carbon that may be distributed from the martensite.

一旦達到淬火溫度(18)，則相對於淬火溫度升高鋼片之溫度或在淬火溫度下維持鋼片之溫度給定時間段。詳言之，此階段可稱作分配階段。在該階段中，鋼片之溫度至少維持在淬火溫度下以允許碳自快速冷卻期間形成的馬氏體擴散且進入任何剩餘的奧氏體。該擴散可允許剩餘的奧氏體在室溫下為穩定的(或介穩定的)，由此改良鋼片之機械性質。 Once the quenching temperature (18) is reached, the temperature of the steel sheet is raised relative to the quenching temperature or the temperature of the steel sheet is maintained at the quenching temperature for a given period of time. In detail, this phase can be called the allocation phase. In this stage, the temperature of the steel sheet is maintained at least at the quenching temperature to allow the carbon to diffuse from the martensite formed during rapid cooling and into any remaining austenite. This diffusion allows the remaining austenite to be stable (or metastable) at room temperature, thereby improving the mechanical properties of the steel sheet.

在一些實施例中，可在高於Ms下加熱鋼片至相對較高分配溫度(20)，且其後將其保持在較高分配溫度(20)下。在此階段期間可採用各種方法加熱鋼片。僅舉例而言，可使用感應加熱、火焰加熱及/或其類似者來加熱鋼片。或者，在其他實施例中，可加熱鋼片但加熱至不同的、稍微低於Ms之較低分配溫度(22)。隨後可同樣保持鋼片在較低分配溫度(22)下某一時間段。在又一第三替代實施例中，在鋼片僅維持在淬火溫度下時可使用另一替代分配溫度(24)。當然，鑒於本文中之教示，對一般技術者而言可使用任何其他適合的分配溫度將變得 顯而易見。 In some embodiments, the steel sheet can be heated to a relatively higher dispensing temperature (20) above M s and thereafter maintained at a higher dispensing temperature (20). Various methods can be used to heat the steel sheet during this stage. By way of example only, induction heating, flame heating, and/or the like can be used to heat the steel sheet. Alternatively, in other embodiments, but may be heated steel sheet is heated to a different, slightly below the lower dispensing temperature (22) M s of. The steel sheet can then be held for a certain period of time at a lower dispensing temperature (22). In yet another third alternative embodiment, another alternative dispensing temperature (24) can be used while the steel sheet is only maintained at the quenching temperature. Of course, any other suitable dispensing temperature that would be apparent to one of ordinary skill would be apparent in view of the teachings herein.

在鋼片已達到需要的分配溫度(20、22、24)之後，將鋼片維持在需要的分配溫度(20、22、24)下充足的時間以允許碳自馬氏體分配至奧氏體。隨後可冷卻鋼片至室溫。 After the steel sheet has reached the required dispensing temperature (20, 22, 24), the steel sheet is maintained at the desired dispensing temperature (20, 22, 24) for a sufficient period of time to allow carbon to be distributed from martensite to austenite. . The steel sheet can then be cooled to room temperature.

圖2顯示上文所述之關於圖1的熱循環替代實施例(用實線(40)顯示典型的鍍鋅/鍍鋅退火熱循環且用虛線顯示自典型的鍍鋅/鍍鋅退火熱循環之偏離)。詳言之，與圖1之製程類似，首先加熱鋼片至最高金屬溫度(42)。在所說明之實施例中的最高金屬溫度(42)顯示為至少高於A1。由此，在最高金屬溫度(42)下，鋼片之至少一部分將轉化成奧氏體。當然，與圖1之製程類似，本發明實施例亦可包括超過A3之最高金屬溫度。 Figure 2 shows an alternative embodiment of the thermal cycle described above with respect to Figure 1 (showing a typical galvanizing/galvanizing annealing thermal cycle with a solid line (40) and showing from a typical galvanizing/galvanizing annealing thermal cycle with dashed lines Deviation). In particular, similar to the process of Figure 1, the steel sheet is first heated to the highest metal temperature (42). In the illustrated embodiment the maximum temperature of the metal in embodiment (42) displays at least higher than A 1. Thus, at the highest metal temperature (42), at least a portion of the steel sheet will be converted to austenite. Of course, the process of FIG. 1 is similar to, embodiments of the present invention may also comprise more than three of A peak metal temperature.

隨後，可快速淬火(44)鋼片。應理解，淬火(44)可足夠快以引發在最高金屬溫度(42)下形成的奧氏體中之一部分轉化成馬氏體，由此避免過量轉化為非馬氏體組份(諸如肥粒鐵、波來鐵、韌鋼及/或其類似者)。 Subsequently, the steel sheet can be quickly quenched (44). It should be understood that quenching (44) may be fast enough to initiate conversion of a portion of the austenite formed at the highest metal temperature (42) to martensite, thereby avoiding excessive conversion to non-martensitic components (such as fertilizer particles). Iron, Bora, tough steel and/or the like).

隨後可在淬火溫度(46)下停止淬火(44)。與圖1之製程類似，淬火溫度(46)低於Ms。當然，低於Ms之量可視所用的材料而變化。然而，如上文所描述，在許多實施例中，淬火溫度(46)與Ms之間的差值可足夠大以形成充足量之馬氏體又足夠低以避免消耗過多奧氏體。 The quenching (44) can then be stopped at the quenching temperature (46). Similar to the process of Figure 1, the quenching temperature (46) is lower than M s . Of course, the amount below M s may vary depending on the material used. However, as described above, in many embodiments, the difference between the quenching temperature (46) and M s may be large enough to form a sufficient amount of martensite is low enough to avoid excessive consumption of austenite.

隨後接著再加熱(48)鋼片至分配溫度(50、52)。不同於圖1之製程，本發明實施例中之分配溫度(50、52)可藉由鍍鋅或鍍鋅退火鋅浴槽溫度表示特徵(若如此使用鍍鋅或鍍鋅退火)。舉例而言，在使用鍍鋅之實施例中，可再加熱鋼片至鍍鋅浴槽溫度(50)，且接著在鍍鋅製程期間保持在此溫度下。在鍍鋅製程期間，可能出現類似於上文所述的分配之分配。由此，鍍鋅浴槽溫度(50)亦可充當分配溫度(50)。同樣，在使用鍍鋅退火之實施例中，除較高浴槽/分配溫度(52)之外，製 程可為實質上相同的。 The steel sheet is then reheated (48) to the dispensing temperature (50, 52). Unlike the process of Figure 1, the dispensing temperature (50, 52) in the embodiments of the present invention can be characterized by galvanizing or galvanizing annealed zinc bath temperatures (if galvanized or galvannealed is used). For example, in an embodiment using galvanizing, the steel sheet can be reheated to a galvanizing bath temperature (50) and then maintained at this temperature during the galvanizing process. During the galvanizing process, an allocation similar to that described above may occur. Thus, the galvanizing bath temperature (50) can also serve as the dispensing temperature (50). Also, in the embodiment using galvannealing, in addition to the higher bath/distribution temperature (52), Cheng can be essentially the same.

最後，允許冷卻(54)鋼片至室溫，在室溫下至少部分來自上文所述之分配步驟之奧氏體可為穩定的(或介穩定的)。 Finally, the steel sheet is allowed to cool (54) to room temperature, and at least a portion of the austenite from the dispensing step described above may be stable (or metastable) at room temperature.

在一些實施例中，鋼片可包括某些合金化添加物以改良鋼片形成主要為奧氏體及馬氏體之微結構之傾向及/或改良鋼片之機械性質。適合的鋼片組份可包括按重量百分比計的以下一或多者：0.15-0.4%碳、1.5-4%錳、0-2%矽或鋁或其部分組合、0-0.5%鉬、0-0.05%鈮、其他附帶元素，且其餘為鐵。 In some embodiments, the steel sheet may include certain alloying additives to improve the tendency of the steel sheet to form a microstructure that is primarily austenitic and martensite and/or to improve the mechanical properties of the steel sheet. Suitable steel sheet components may include one or more of the following: 0.15-0.4% carbon, 1.5-4% manganese, 0-2% niobium or aluminum or a partial combination thereof, 0-0.5% molybdenum, 0 -0.05% bismuth, other incidental elements, and the balance being iron.

另外，在其他實施例中，適合的鋼片組份可包括按重量百分比計的以下一或多者：0.15%-0.5%碳、1%-3%錳、0-2%矽或鋁或其部分組合、0-0.5%鉬、0-0.05%鈮、其他附帶元素，且其餘為鐵。另外，除鈮之外或代替鈮，其他實施例可包括釩及/或鈦之添加物，但該等添加物完全為視情況選用的。 Additionally, in other embodiments, suitable steel sheet components can include one or more of the following: 0.15%-0.5% carbon, 1%-3% manganese, 0-2% niobium or aluminum or Partial combination, 0-0.5% molybdenum, 0-0.05% bismuth, other incidental elements, and the balance being iron. Additionally, other embodiments may include vanadium and/or titanium additions in addition to or instead of niobium, but such additives are entirely optional.

在一些實施例中，碳之合金化添加物可用以穩定奧氏體。舉例而言，增加碳可降低Ms溫度，降低其他非馬氏體組份(例如韌鋼、肥粒鐵、波來鐵)之轉化溫度，且增加形成非馬氏體產物所需要的時間。另外，碳添加物可改良材料之可硬化性，由此保持非馬氏體組份在可局部降低冷卻速率之材料中心處形成。然而，應理解碳添加物可能為受限制的，因為大量碳添加物可能會對可焊性產生有害影響。 In some embodiments, an alloying alloy of carbon can be used to stabilize the austenite. For example, increasing carbon reduces the temperature of M s , lowers the conversion temperature of other non-martensitic components (eg, tough steel, ferrite, and ferrite) and increases the time required to form non-martensitic products. Additionally, the carbon additive can improve the hardenability of the material, thereby maintaining the non-martensitic component formed at the center of the material where the cooling rate can be locally reduced. However, it should be understood that carbon additions may be limited because large amounts of carbon additives may have a detrimental effect on solderability.

在一些實施例中，可添加錳之合金化添加物以藉由降低如上文所描述之其他非馬氏體組份之轉化溫度來提供奧氏體之額外穩定。錳添加物可藉由提高可硬化性來進一步改良鋼片形成主要為奧氏體與馬氏體之微結構之傾向。 In some embodiments, an alloying additive of manganese may be added to provide additional stabilization of austenite by reducing the conversion temperature of other non-martensitic components as described above. The manganese additive can further improve the tendency of the steel sheet to form a microstructure mainly composed of austenite and martensite by improving hardenability.

在其他實施例中，鉬之合金化添加物可用以提高可硬化性。 In other embodiments, alloying additives of molybdenum may be used to increase hardenability.

在其他實施例中，可添加矽及/或鋁之合金化添加物以減少碳化物之形成。應理解，在一些實施例中可能需要減少碳化物形成，因為 碳化物之存在可能降低可用於擴散進入奧氏體的碳之含量。由此，矽及/或鋁添加物可用以在室溫下進一步穩定奧氏體。 In other embodiments, an alloying additive of niobium and/or aluminum may be added to reduce the formation of carbides. It should be understood that in some embodiments it may be desirable to reduce carbide formation because The presence of carbides may reduce the amount of carbon available for diffusion into the austenite. Thus, niobium and/or aluminum additives can be used to further stabilize the austenite at room temperature.

在一些實施例中，鎳、銅及鉻添加物可用以穩定奧氏體。舉例而言，該等元素可能引起Ms溫度降低。另外，鎳、銅及鉻可進一步提高鋼片之可硬化性。 In some embodiments, nickel, copper, and chromium additions can be used to stabilize the austenite. For example, such elements may cause a decrease in the temperature of M s . In addition, nickel, copper and chromium can further improve the hardenability of the steel sheet.

在一些實施例中，鈮之合金化添加物(或其他微合金化元素，諸如鈦、釩及/或其類似者)可用以提高鋼片之機械性質。舉例而言，鈮可經由由碳化物形成所得到的晶界釘紮增加鋼片之強度。 In some embodiments, an alloying additive of bismuth (or other microalloying elements such as titanium, vanadium, and/or the like) can be used to increase the mechanical properties of the steel sheet. For example, niobium can increase the strength of the steel sheet via grain boundary pinning obtained by carbide formation.

在其他實施例中，可對合金化元素之濃度及選定的用於合金化之元素進行變化。當然，當進行該等變化時，應理解該等變化可能對鋼片微結構及/或機械性質(根據各給定合金化添加物之上文所述的性質)具有需要的或不良的影響。 In other embodiments, the concentration of the alloying elements and the selected elements for alloying can be varied. Of course, when such changes are made, it is understood that such variations may have a desired or undesirable effect on the microstructure and/or mechanical properties of the steel sheet (according to the properties described above for each given alloying additive).

實例1Example 1

使用闡述在下表1中之組份製備鋼片之實施例。 An example of preparing a steel sheet using the components set forth in Table 1 below was used.

根據以下參數在實驗室設備上加工材料。使用銅冷卻的楔形手柄及凹穴顎式夾具使各樣品經受Gleeble 1500處理，該等處理。在1100℃下奧氏體化樣品，且隨後以在1℃/s-100℃/s之間的各種冷卻速率冷卻至室溫。 The material is processed on laboratory equipment according to the following parameters. Each sample was subjected to Gleeble 1500 treatment using copper-cooled wedge handles and pocket clamps. The sample was austenitized at 1100 ° C and then cooled to room temperature at various cooling rates between 1 ° C / s - 100 ° C / s.

實例2Example 2

在各樣品的表面上取得描述於上文實例1及表1中之鋼組份中的每一者之洛氏硬度。測試之結果繪製於圖3至圖5中，繪製洛氏硬度作為冷卻速率的函數。對於各數據點顯示至少七個量測值之平均值。組份V4037、V4038及V4039分別對應於圖3、圖4及圖5。 The Rockwell hardness of each of the steel components described in Examples 1 and 1 above was obtained on the surface of each sample. The results of the tests are plotted in Figures 3 through 5, and Rockwell hardness is plotted as a function of cooling rate. An average of at least seven measurements is displayed for each data point. Components V4037, V4038, and V4039 correspond to Figures 3, 4, and 5, respectively.

實例3Example 3

在軸向中經過厚度方向在接近實例1之組份中之每一者之各樣品的中心處取得光學顯微圖。此等測試之結果顯示於圖6至圖8中。組份V4037、V4038及V4039分別對應於圖6、圖7及圖8。另外，圖6至圖8各含有對於各組份之六個顯微圖，各顯微圖表示經受不同冷卻速率之樣品。 Optical micrographs were taken in the axial direction through the thickness direction at the center of each sample close to each of the components of Example 1. The results of these tests are shown in Figures 6-8. Components V4037, V4038, and V4039 correspond to Figures 6, 7, and 8, respectively. In addition, Figures 6 through 8 each contain six micrographs for each component, each micrograph representing a sample that is subjected to different cooling rates.

實例4Example 4

根據本文所述之程序使用實例2及3的數據估算實例1之組份中之每一者的臨界冷卻速率。本文中之臨界冷卻速率係指形成馬氏體及最小化非馬氏體轉化產物之形成所需的冷卻速率。此等測試之結果如下：V4037：70℃/s The critical cooling rates for each of the components of Example 1 were estimated using the data of Examples 2 and 3 according to the procedures described herein. The critical cooling rate herein refers to the cooling rate required to form martensite and minimize the formation of non-martensitic conversion products. The results of these tests are as follows: V4037: 70 ° C / s

V4038：75℃/s V4038: 75 ° C / s

V4039：7℃/s V4039: 7 ° C / s

實例5Example 5

使用闡述在下表2中之組份製備鋼片之實施例。 An example of preparing a steel sheet using the components set forth in Table 2 below was used.

藉由熔化、熱軋製及冷軋製加工材料。隨後對材料進行更詳細地描述於下文實例6-7中之測試。除意欲以上文所述的根據圖1之製程使用V4039之外，意欲以上文所述之根據圖2之製程使用全部列於表2中之組份。熱V4039具有意欲提供較高可硬化性之組份，該組份依據上文所述之根據圖1之熱分佈所需來提供較高可硬化性。因此在熱軋 製之後但在冷軋製之前，在600℃下在100% H2氣氛中使V4039經受退火2小時。在冷軋製期間全部材料減小約75%至1mm。闡述於表2中的材料組份之一部分在熱軋製及冷軋製之後的結果分別顯示於表3及表4中。 The material is processed by melting, hot rolling and cold rolling. The materials are then described in more detail in the tests in Examples 6-7 below. Except for the use of V4039 according to the process of Figure 1 described above, it is intended that the processes according to Figure 2 described above use all of the components listed in Table 2. Heat V4039 has a component intended to provide a higher hardenability which provides higher hardenability in accordance with the heat distribution according to Figure 1 described above. Thus, after hot rolling but before cold rolling, V4039 was subjected to annealing at 600 ° C for 2 hours in a 100% H 2 atmosphere. All materials are reduced by about 75% to 1 mm during cold rolling. The results of hot rolling and cold rolling of one of the material components described in Table 2 are shown in Tables 3 and 4, respectively.

實例7Example 7

使實例5之組份經受Gleeble膨脹測量法。在真空中使用101.6×25.4×1mm之樣品在25.4mm方向中以c應變計量測膨脹進行Gleeble膨脹測量。產生所得的膨脹相對於溫度之曲線。擬合膨脹測量數據之線段且將膨脹測量數據自線形特性偏離處之點視為所關注之轉化溫度(例如A1、A3、Ms)。所得轉化溫度列表於表5中。 The components of Example 5 were subjected to Gleeble expansion measurement. Gleeble expansion measurements were performed in a vacuum using a sample of 101.6 x 25.4 x 1 mm in the 25.4 mm direction with c strain measurement expansion. A resulting curve of the expansion versus temperature is produced. Fitting the expansion line of the measurement data and the measurement data from the expansion point of the deviation from the linear characteristic transition temperature considered (e.g. A1, A3, M s) of interest. The resulting conversion temperatures are listed in Table 5.

Gleeble方法亦用於量測實例5之組份中之每一者的臨界冷卻速率。如上文所描述，第一方法採用Gleeble膨脹測量法。第二方法採用洛氏硬度之量測值。詳言之，在以一系列冷卻速率使樣品經受Gleeble測試之後，取得洛氏硬度量測值。由此，利用對於一系列冷卻速率之硬度量測值獲得各材料組份之洛氏硬度量測值。隨後將給定組份在各冷卻速率下的洛氏硬度量測值之間進行比較。2點HRA之洛氏硬度偏差被視為顯著的。將避免非馬氏體轉化產物之臨界冷卻速率視為最高冷卻速率，對於該最高冷卻速率，硬度比最大硬度低2點HRA。所得的對於列於實例5中之組份中之一部分的臨界冷卻速率亦列表於表5中。 The Gleeble method was also used to measure the critical cooling rate for each of the components of Example 5. As described above, the first method employs the Gleeble expansion measurement. The second method uses a measure of Rockwell hardness. In particular, the Rockwell hardness measurements were taken after the samples were subjected to the Gleeble test at a series of cooling rates. Thus, the Rockwell hardness measurements of the various material components are obtained using hardness measurements for a range of cooling rates. The given components are then compared between Rockwell hardness measurements at various cooling rates. The Rockwell hardness deviation of the 2 point HRA is considered significant. The critical cooling rate of the non-martensitic conversion product is avoided as the highest cooling rate for which the hardness is 2 HRA lower than the maximum hardness. The resulting critical cooling rates for one of the components listed in Example 5 are also listed in Table 5.

實例8Example 8

使用實例5之組份計算淬火溫度及殘留奧氏體之理論最高值。使 用上文所述之Speer等人之方法進行計算。對於列於實例5中之組份中之一部分的計算結果列表於下表6中。 The quenching temperature and the theoretical maximum value of retained austenite were calculated using the components of Example 5. Make Calculations were performed using the method of Speer et al., supra. The calculation results for one of the components listed in Example 5 are listed in Table 6 below.

實例9Example 9

使實例5之組份之樣品經受顯示於圖1及圖2中的熱分佈(在給定組份之樣品之間變化最高金屬溫度及淬火溫度)。如上文所描述，僅使組份V4039經受顯示於圖1中之熱分佈，而使全部其他組份經受顯示於圖2中之熱循環。取得各樣品之拉伸強度量測值。所得的拉伸量測值繪製於圖9至圖12中。詳言之，圖9至圖10顯示相對於奧氏體化溫度繪製的拉伸強度數據及圖11至圖12顯示相對於淬火溫度繪製的拉伸強度數據。另外，當使用Gleeble方法進行熱循環時，該等數據點係使用「Gleehle」指示。類似地，當使用鹽浴槽進行熱循環時，該等數據點係使用「鹽」指示。 The samples of the components of Example 5 were subjected to the heat distribution shown in Figures 1 and 2 (the highest metal temperature and quenching temperature were varied between samples of a given composition). As described above, only component V4039 is subjected to the heat distribution shown in Figure 1, while all other components are subjected to the thermal cycle shown in Figure 2. The tensile strength measurements of each sample were obtained. The resulting tensile measurements are plotted in Figures 9-12. In detail, FIGS. 9 to 10 show tensile strength data plotted against austenitizing temperature and FIGS. 11 to 12 show tensile strength data plotted against quenching temperature. In addition, when the Gleeble method is used for thermal cycling, the data points are indicated by "Gleehle". Similarly, when a salt bath is used for thermal cycling, the data points are indicated using "salt."

另外，列於實例5中之各組份之類似的拉伸量測值(當可獲得時)列表於下文所顯示的表7中。分配時間及溫度僅為舉例而顯示，在其他實施例中，機制(諸如碳分配及/或相轉化)在非等溫加熱及冷卻至規定的分配溫度(該分配溫度亦可有助於最終材料特性)或自規定的分配溫度非等溫加熱及冷卻期間發生。 In addition, similar tensile measurements (when available) for each of the components listed in Example 5 are listed in Table 7 shown below. The dispensing time and temperature are shown by way of example only. In other embodiments, mechanisms such as carbon partitioning and/or phase inversion are non-isothermally heated and cooled to a specified dispensing temperature (the dispensing temperature may also contribute to the final material). Characteristics) or occurs during specified non-isothermal heating and cooling of the dispensed temperature.

表7-分配後之拉伸數據Table 7 - Stretched data after allocation

應理解，可對本發明進行各種修改而不背離其精神及範疇。因此，應根據所附申請專利範圍確定本發明之限制。 It will be appreciated that various modifications may be made to the invention without departing from the spirit and scope. Accordingly, the limitations of the invention should be determined in accordance with the scope of the appended claims.

10‧‧‧熱浸漬鍍鋅或鍍鋅退火熱分佈 10‧‧‧Hot-dip galvanizing or galvanizing annealing heat distribution

12‧‧‧最高金屬溫度 12‧‧‧Highest metal temperature

14‧‧‧恆定溫度 14‧‧‧ Constant temperature

16‧‧‧鍍鋅退火溫度 16‧‧‧galvanizing annealing temperature

18‧‧‧淬火溫度 18‧‧‧Quenching temperature

20‧‧‧較高分配溫度 20‧‧‧Higher distribution temperature

22‧‧‧較低分配溫度 22‧‧‧lower distribution temperature

24‧‧‧替代分配溫度 24‧‧‧Alternative distribution temperature

Claims (7)

一種加工鋼片之方法，該鋼片包含按重量百分比計的以下元素：0.15-0.5%碳；1-3%錳；2%或更少之矽、鋁或其部分組合；0.5%或更少之鉬；0.05%或更少之鈮；及其餘為鐵及其他附帶雜質；該方法包含：(a)加熱該鋼片至第一溫度(T1)，其中T1至少高於該鋼片轉化成奧氏體(austenite)及肥粒鐵(ferrite)的溫度；(b)藉由以一冷卻速率冷卻使該鋼片冷卻至第二溫度(T2)，其中T2低於馬氏體(martensite)起始溫度(Ms)，其中該冷卻速率足夠快以使奧氏體轉化成馬氏體；(c)再加熱該鋼片至分配溫度，其中該分配溫度足以允許碳在該鋼片之結構內擴散；(d)藉由將該鋼片在該分配溫度下保持一保持時間來穩定奧氏體，其中該保持時間為足以允許碳自馬氏體擴散至奧氏體之時間段；及(e)冷卻該鋼片至室溫。 A method of processing a steel sheet comprising the following elements by weight percent: 0.15-0.5% carbon; 1-3% manganese; 2% or less of bismuth, aluminum or a partial combination thereof; 0.5% or less Molybdenum; 0.05% or less of bismuth; and the balance being iron and other incidental impurities; the method comprises: (a) heating the steel sheet to a first temperature (T1), wherein T1 is at least higher than the steel sheet is converted into Austrian The temperature of the austenite and ferrite; (b) cooling the steel sheet to a second temperature (T2) by cooling at a cooling rate, wherein T2 is lower than the martensite start Temperature (M s ), wherein the cooling rate is fast enough to convert austenite to martensite; (c) reheating the steel sheet to a dispensing temperature, wherein the dispensing temperature is sufficient to allow carbon to diffuse within the structure of the steel sheet (d) stabilizing the austenite by maintaining the steel sheet at the dispensing temperature for a holding time, wherein the holding time is a period sufficient to allow diffusion of carbon from martensite to austenite; and (e) The steel sheet was cooled to room temperature. 如請求項1之方法，其進一步包含熱浸漬鍍鋅或鍍鋅退火同時穩定奧氏體。 The method of claim 1, further comprising hot dip galvanizing or galvanizing annealing while stabilizing austenite. 如請求項2之方法，其中該熱浸漬鍍鋅或鍍鋅退火在高於Ms下進行。 The method of claim 2, wherein the hot dip galvanizing or galvanizing annealing is performed above M s . 如請求項1之方法，其中該分配溫度高於Ms。 The method of claim 1, wherein the distribution temperature is higher than M s . 如請求項1之方法，其中該鋼片包含按重量百分比計的以下元素：0.15-0.4%碳；1.5-4%錳；2%或更少之矽、鋁或其部分組合；0.5%或更少之鉬；0.05%或更少之鈮；及其餘為鐵及其他附帶雜質。 The method of claim 1, wherein the steel sheet comprises the following elements by weight percent: 0.15-0.4% carbon; 1.5-4% manganese; 2% or less of bismuth, aluminum or a partial combination thereof; 0.5% or more Less molybdenum; 0.05% or less; and the rest are iron and other incidental impurities. 一種加工鋼片之方法，該鋼片包含經選定之組成，其包含按重量百分比計的以下元素：0.15-0.5%碳；1-3%錳；2%或更少之矽、鋁或其部分組合；0.5%或更少之鉬；0.05%或更少之鈮；及其餘為鐵及其他附帶雜質；該方法包含：(a)加熱該鋼片至第一溫度(T1)，其中T1至少高於該鋼片轉化成奧氏體及肥粒鐵的溫度；(b)藉由以或高於一臨界冷卻速率冷卻使該鋼片冷卻至第二溫度(T2)，其中T2低於馬氏體起始溫度(Ms)，其中該臨界冷卻速率足夠快以使奧氏體轉化成馬氏體，其中該臨界冷卻速率係由該鋼片之該經選定組成藉由一冷卻速率所導致該鋼片之室溫硬度不低於該鋼片之最大室溫硬度之2 HRA以下所定義；(c)再加熱該鋼片至分配溫度，其中該分配溫度足以允許碳在 該鋼片之結構內擴散；(d)藉由將該鋼片在該分配溫度下保持一保持時間來穩定奧氏體，其中該保持時間為足以允許碳自馬氏體擴散至奧氏體之時間段；及(e)冷卻該鋼片至室溫。 A method of processing a steel sheet comprising a selected composition comprising the following elements by weight percent: 0.15-0.5% carbon; 1-3% manganese; 2% or less of bismuth, aluminum or a portion thereof Combination; 0.5% or less molybdenum; 0.05% or less of bismuth; and the balance being iron and other incidental impurities; the method comprising: (a) heating the steel sheet to a first temperature (T1), wherein T1 is at least high Converting the steel sheet to austenite and ferrite iron; (b) cooling the steel sheet to a second temperature (T2) by cooling at or above a critical cooling rate, wherein T2 is lower than martensite An initial temperature (M s ), wherein the critical cooling rate is fast enough to convert austenite to martensite, wherein the critical cooling rate is caused by the selected composition of the steel sheet by a cooling rate The room temperature hardness of the sheet is not less than 2 HRA below the maximum room temperature hardness of the steel sheet; (c) reheating the steel sheet to a distribution temperature, wherein the distribution temperature is sufficient to allow carbon to diffuse within the structure of the steel sheet (d) stabilizing the austenite by maintaining the steel sheet at the dispensing temperature for a holding time, wherein the holding time is To allow the diffusion of carbon from the martensite to austenite period of time; and (e) cooling the steel to room temperature. 一種加工鋼片之方法，該鋼片包含按重量百分比計的以下元素：0.15-0.5%碳；1-3%錳；2%或更少之矽、鋁或其部分組合；0.5%或更少之鉬；0.05%或更少之鈮；及其餘為鐵及其他附帶雜質；該方法包含：(a)加熱該鋼片至第一溫度(T1)，其中T1至少高於該鋼片轉化成奧氏體及肥粒鐵的溫度；(b)藉由以一冷卻速率冷卻使該鋼片冷卻至第二溫度(T2)，其中T2低於馬氏體起始溫度(Ms)，其中該冷卻速率足夠快以使奧氏體轉化成馬氏體，其中該冷卻速率足夠快以實質地抑制韌鋼(bainite)及其他非馬氏體轉化產物之形成；(c)再加熱該鋼片至分配溫度，其中該分配溫度足以允許碳在該鋼片之結構內擴散；(d)藉由將該鋼片在該分配溫度下保持一保持時間來穩定奧氏體，其中該保持時間為足以允許碳自馬氏體擴散至奧氏體之時間段；及(e)冷卻該鋼片至室溫。 A method of processing a steel sheet comprising the following elements by weight percent: 0.15-0.5% carbon; 1-3% manganese; 2% or less of bismuth, aluminum or a partial combination thereof; 0.5% or less Molybdenum; 0.05% or less of bismuth; and the balance being iron and other incidental impurities; the method comprises: (a) heating the steel sheet to a first temperature (T1), wherein T1 is at least higher than the steel sheet is converted into Austrian The temperature of the ferrite and the ferrite iron; (b) cooling the steel sheet to a second temperature (T2) by cooling at a cooling rate, wherein T2 is lower than the martensite start temperature (M s ), wherein the cooling The rate is fast enough to convert austenite to martensite, wherein the cooling rate is fast enough to substantially inhibit the formation of bainite and other non-martensitic transformation products; (c) reheat the steel sheet to distribution a temperature, wherein the dispensing temperature is sufficient to allow carbon to diffuse within the structure of the steel sheet; (d) stabilizing the austenite by maintaining the steel sheet at the dispensing temperature for a holding time, wherein the holding time is sufficient to allow carbon a period of time from the diffusion of martensite to austenite; and (e) cooling the steel sheet to room temperature.
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