TWI627288B - 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熱處理之製造方法 - Google Patents
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熱處理之製造方法 Download PDFInfo
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- austenite
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 72
- 239000010959 steel Substances 0.000 title claims abstract description 72
- 238000000034 method Methods 0.000 title claims abstract description 38
- 238000010438 heat treatment Methods 0.000 title claims description 5
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 title description 6
- 239000011701 zinc Substances 0.000 title description 6
- 229910052725 zinc Inorganic materials 0.000 title description 6
- 238000004519 manufacturing process Methods 0.000 title description 5
- 230000001747 exhibiting effect Effects 0.000 title description 3
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 50
- 238000001816 cooling Methods 0.000 claims abstract description 39
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 38
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 24
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 24
- 230000015572 biosynthetic process Effects 0.000 claims abstract description 11
- 230000009466 transformation Effects 0.000 claims abstract description 6
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 239000011733 molybdenum Substances 0.000 claims abstract description 5
- 238000009826 distribution Methods 0.000 claims description 39
- 238000005246 galvanizing Methods 0.000 claims description 30
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 239000010955 niobium Substances 0.000 claims description 6
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 239000010703 silicon Substances 0.000 claims description 5
- 229910000859 α-Fe Inorganic materials 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 238000009792 diffusion process Methods 0.000 claims description 3
- 239000011572 manganese Substances 0.000 claims description 3
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 claims description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 238000012545 processing Methods 0.000 claims description 2
- 230000000087 stabilizing effect Effects 0.000 claims description 2
- 230000014759 maintenance of location Effects 0.000 claims 2
- 239000012535 impurity Substances 0.000 claims 1
- 238000003303 reheating Methods 0.000 claims 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 abstract description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 239000011651 chromium Substances 0.000 abstract description 3
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 239000010949 copper Substances 0.000 abstract description 3
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract description 3
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 238000005382 thermal cycling Methods 0.000 abstract description 3
- 230000007246 mechanism Effects 0.000 abstract description 2
- 238000010791 quenching Methods 0.000 description 46
- 230000000171 quenching effect Effects 0.000 description 46
- 230000008569 process Effects 0.000 description 20
- 239000000654 additive Substances 0.000 description 17
- 229910052751 metal Inorganic materials 0.000 description 14
- 239000002184 metal Substances 0.000 description 14
- 238000005275 alloying Methods 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 238000000137 annealing Methods 0.000 description 9
- 238000006243 chemical reaction Methods 0.000 description 5
- 238000007542 hardness measurement Methods 0.000 description 5
- 238000005259 measurement Methods 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000007572 expansion measurement Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000005244 galvannealing Methods 0.000 description 2
- 230000014509 gene expression Effects 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- 150000003839 salts Chemical class 0.000 description 2
- 238000000638 solvent extraction Methods 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 238000010961 commercial manufacture process Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000003337 fertilizer Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000000879 optical micrograph Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
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- 230000004044 response Effects 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
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Abstract
本發明係關於具有高強度與良好成形性的鋼，其係以用於在該鋼中形成奧氏體(austcnitic)與馬氏體(martensitic)微結構之組份及方法製造。碳、錳、鉬、鎳、銅及鉻可藉由諸如降低非馬氏體組份之轉化溫度及/或提高鋼之可硬化性之機制來促進形成室溫穩定的(或介穩定的)奧氏體(austenite)。利用在低於馬氏體起始溫度下快速冷卻之後再加熱之熱循環可藉由允許碳自馬氏體擴散進入奧氏體來促進形成室溫穩定的奧氏體。
Description
本申請案主張臨時專利申請案第61/824,699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61/824,699號之揭示內容以引用的方式併入本文中。
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。
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。
10‧‧‧熱浸漬鍍鋅或鍍鋅退火熱分佈
12‧‧‧最高金屬溫度
14‧‧‧恆定溫度
16‧‧‧鍍鋅退火溫度
18‧‧‧淬火溫度
20‧‧‧較高分配溫度
22‧‧‧較低分配溫度
24‧‧‧替代分配溫度
40‧‧‧實線
42‧‧‧最高金屬溫度
44‧‧‧淬火
46‧‧‧淬火溫度
48‧‧‧再加熱
50‧‧‧鍍鋅浴槽溫度/分配溫度
52‧‧‧浴槽/分配溫度
54‧‧‧冷卻
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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。
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))。
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)。
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。
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()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
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。
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。
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。
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。
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。
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)。
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。
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。
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)。
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。
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。
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。
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。
在其他實施例中，鉬之合金化添加物可用以提高可硬化性。
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。
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。
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。
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。
使用闡述在下表1中之組份製備鋼片之實施例。
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。
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。
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。
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
V4038：75℃/s
V4039：7℃/s
使用闡述在下表2中之組份製備鋼片之實施例。
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。
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。
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。
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。
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「Gleeble」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。
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。
表7-分配後之拉伸數據
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。
Claims (6)
- 一種加工經選定組成之鋼片之方法，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，其中對於該經選定組成之該鋼片之該冷卻速率係藉由臨界冷卻速率來定義，該臨界冷卻速率導致該鋼片之室溫硬度不低於該鋼片之最高室溫硬度2 HRA以下，以避免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。
- 如請求項1之方法，其進一步包含熱浸漬鍍鋅或鍍鋅退火該鋼片同時冷卻該鋼片至T2。
- 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。
- 如請求項1之方法，其中該分配溫度高於Ms。
- 如請求項1之方法，其中該分配溫度低於Ms。
- 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。
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| CN109554621B (zh) * | 2018-12-03 | 2020-11-27 | 东北大学 | 一种低密度Fe-Mn-Al-C热轧Q＆P钢及其制造方法 |
| CN109554622B (zh) * | 2018-12-03 | 2020-12-04 | 东北大学 | 淬火至贝氏体区获得Q＆P组织的热轧Fe-Mn-Al-C钢及制造方法 |
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