TW201925495A - 具特製性質之加壓硬化鋼 - Google Patents
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Abstract
本發明提供一種由兩種鋼製成之特製熔接坯料,一種鋼為合金A之鋼且一種鋼為合金B之鋼。合金A包含0.10-0.50重量% C、0.1-0.5重量% Si、2.0-8.0重量% Mn、0.0-6.0重量% Cr、0.0-2.0重量% Mo、0.0-0.15重量% Ti及0.0-0.005重量% B,且其中合金B包含0.06-0.12重量% C、0.1-0.25重量% Si、1.65-2.42重量% Mn、0.0-0.70重量% Cr、0.08-0.40重量% Mo、0.0-0.05重量% V及0.01-0.05重量% Ti。
Description
本發明係關於包含合金A及合金B之特製熔接坯料。本發明亦提供一種製造特製熔接坯料之方法。
加壓硬化鋼藉由熱衝壓過程製造,其中鋼在高溫下變形,在該高溫下沃斯田鐵為穩定的,且隨後在衝壓模具中以足夠的冷卻速率淬火以形成麻田散體(martensite)。此等鋼通常用於需要高強度及高耐侵入性之汽車應用中之結構部件。具有特製性質之加壓硬化鋼對該等應用具有吸引力,因為由於組件中相對硬及軟的區域,其除了高能量吸收以外,還可提供高耐侵入性。特製性質可藉由使用特製熔接坯料獲得,其為由兩種具有不同組成或厚度之鋼片構成之坯料。
典型商業加壓硬化鋼(例如22MnB5)之極限抗張強度為大約1500 MPa,總伸長率為大約6-8%。習知加壓硬化鋼片可接合至具有較低硬化度之鋼及加壓硬化後轉化為更軟的微觀結構(極限抗張強度為大約700 MPa)之鋼。鋼之此組合通常稱為特製熔接坯料(tailor-welded blank,TWB)。加壓硬化TWB產生具有特製性質之組件,其在需要耐侵入性之區域中具有高強度及相對低伸長率之區域,且在需要能量吸收之區域中具有較低強度及較高伸長率之區域。
本發明組合物可用於加壓硬化鋼、熱壓成型鋼、熱衝壓鋼或經加熱至沃斯田體化(austenitizing)溫度、在衝壓模具中成型且隨後淬火以達成衝壓組件之所需最終性質之任何其他鋼。當前申請案描述特製熔接坯料,其由以下構成:高合金鋼,其在加壓硬化後可呈現極高強度(至多2,000 MPa);及較低合金化鋼,其可呈現更中等的強度(至多1,000 MPa)及較高伸長率(至多20%)。
本申請案主張2017年11月2日申請之標題為「Press Hardened Steel with Tailored Properties」之美國臨時專利申請案第62/580,591號的優先權,其揭示內容以引用之方式併入本文中。
特製熔接坯料包含較高合金化鋼(合金A)及較低合金化鋼(合金B)。加壓硬化後,合金A形成呈現與合金B相比較高的強度之微觀結構。在一些實施例中,在一些加壓硬化條件下,合金A之總伸長率可超過加壓硬化後合金B之總伸長率。
合金A及合金B可各自使用習知製鋼、粗加工及精整方法製備。合金A及合金B之實施例可各自為裸露的或經塗佈。合金A及合金B之實施例可藉由雷射熔接或其他已知接合技術來接合以形成特製熔接坯料。在加壓硬化期間,將TWB加熱至高於合金A之較低臨界溫度(Ac1
)之溫度,轉移至模具,模具中形成且隨後冷卻以達成所需最終性質。給定鋼組成之Ac1
溫度為對應於肥粒鐵+滲碳體階段領域與沃斯田鐵+肥粒鐵或肥粒鐵+滲碳體階段領域之間之邊界的溫度。合金A之各組成之Ac1
溫度可藉由此項技術中已知之計算或例如藉由膨脹測量法憑經驗來測定。此項技術中已知之計算包括以下三個例示性計算:
等式1: [1]
等式2: [2]
等式3: [3]
另外,在加壓硬化期間,亦可將TWB加熱至高於合金A之較高臨界溫度(Ac3
)之溫度,轉移至模具中,在模具中成形且隨後冷卻以達成所需最終性質。給定鋼組成之Ac3
溫度為對應於肥粒鐵+沃斯田鐵階段領域與沃斯田鐵階段領域之間之邊界的溫度。合金A之各組成之Ac3
溫度可藉由此項技術中已知之計算或例如藉由膨脹測量法憑經驗來測定。此項技術中已知之計算包括以下例示性計算:
等式4: [4]
合金A採用新穎合金策略,其使用取代元素以藉由取代溶質強化與降低由自發回火造成之軟化的組合增加麻田散體之強度。由自發回火造成之軟化藉由抑制麻田散體起始溫度藉由合金化降至最低。由於由錳、鉻、鉬及鈮之不同添加而產生所提出組合物之硬化度提高,新穎組合物准許實質上不含硼之加壓硬化鋼。
合金B採用合金策略以使此合金之跨臨界溫度可與較高合金化合金A之溫度重疊或與對應於合金A之完全沃斯田體化之溫度重疊。因此,加壓硬化後,合金B之微觀結構主要為肥粒鐵、韌鋼及麻田散體之混合物。
添加碳來降低麻田散體起始溫度、提供固溶體強化及增加鋼之硬化度。碳為沃斯田鐵穩定劑。在合金A之某些實施例中,碳可以0.1-0.50重量%之濃度存在;在其他實施例中,碳可以0.1-0.35重量%之濃度存在;且在再其他實施例中,碳可以約0.22-0.25重量%之濃度存在。在合金B之某些實施例中,碳可以0.06-0.12重量%之濃度存在;在其他實施例中,碳可以0.08-0.1重量%之濃度存在;在其他實施例中,碳可以0.09-0.12重量%之濃度存在;且在再其他實施例中,碳可以0.06-0.085重量%之濃度存在。
添加錳來降低麻田散體起始溫度、提供固溶體強化及增加鋼之硬化度。錳為沃斯田鐵穩定劑。在合金A之某些實施例中,錳可以2.0-8.0重量%之濃度存在;在其他實施例中,錳可以2.0-5.0重量%之濃度存在;在再其他實施例中,錳可以3.0重量%-8.0重量%之濃度存在;且在再其他實施例中,錳可以大於3.0重量%-5.0重量%之濃度存在。在合金B之某些實施例中,錳可以1.65-2.45重量%之濃度存在;在其他實施例中,錳可以2.2-2.45重量%之濃度存在;在其他實施例中,錳可以1.70-1.95重量%之濃度存在,且在再其他實施例中,錳可以1.65-1.85重量%之濃度存在。
添加矽以提供固溶體強化。矽為肥粒鐵穩定劑。在合金A之某些實施例中,矽可以0.1-0.5重量%之濃度存在;在其他實施例中,矽可以0.2-0.3重量%之濃度存在。在合金B之某些實施例中,矽可以0.1-0.25重量%之濃度存在;在其他實施例中,矽可以0.1-0.2重量%之濃度存在;且在其他實施例中,矽可以0.15-0.25重量%之濃度存在。
添加鉬以提供固溶體強化、增加鋼之硬化度、提供微觀結構優化及防止脆化。在合金A之某些實施例中,鉬可以0-2.0重量%之濃度存在;在其他實施例中,鉬可以0.0-0.6重量%之濃度存在;在再其他實施例中,鉬可以0.1-2.0重量%之濃度存在;在其他實施例中,鉬可以0.1-0.6重量%之濃度存在;且在又其他實施例中,鉬可以0.4-0.5重量%之濃度存在。在合金B之某些實施例中,鉬可以0.08-0.4重量%之濃度存在;在其他實施例中,鉬可以0.08-0.15重量%之濃度存在;在再其他實施例中,鉬可以0.12-0.24重量%之濃度存在;且在再其他實施例中,鉬可以0.14-0.25重量%之濃度存在。
可添加鉻來降低麻田散體起始溫度、提供固溶體強化及增加鋼之硬化度。鉻為肥粒鐵穩定劑。在合金A之某些實施例中,鉻可以0-6.0重量%之濃度存在;在其他實施例中,鉻可以2.0-6.0重量%之濃度存在;在其他實施例中,鉻可以0.2-6.0重量%之濃度存在;且在其他實施例中,鉻可以0.2-3.0重量%之濃度存在。在合金B之某些實施例中,鉻可以0.0-0.7重量%之濃度存在;在其他實施例中,鉻可以0.5-0.7重量%之濃度存在;在其他實施例中,鉻可以0.15-0.35重量%之濃度存在;且在其他實施例中,鉻可以0-0.1重量%之濃度存在。
可添加鈮以增加強度及改進鋼之硬化度。在一些實施例中,亦可添加鈮以提供改進之晶粒細化。在合金A及B之某些實施例中,鈮可以0-0.1重量%之濃度存在;在其他實施例中,鈮可以0.01-0.1重量%之濃度存在;且在其他實施例中,鈮可以0.001-0.055重量%之濃度存在。在合金B之某些實施例中,鈮可以0.0-0.1重量%之濃度存在;在其他實施例中,鈮可以0.03-0.05重量%之濃度存在;在其他實施例中,鈮可以0.025-0.055重量%之濃度存在;且在再其他實施例中,鈮可以0.0-0.01重量%之濃度存在。
可添加釩以增加強度且改進鋼之硬化度。在合金A之某些實施例中,釩可以0-0.15重量%之濃度存在;且在其他實施例中,釩可以0.01-0.15重量%之濃度存在。在合金B之某些實施例中,釩可以0.0-0.05重量%之濃度存在;在其他實施例中,釩可以0-0.01重量%之濃度存在;且在其他實施例中,釩可以0.02-0.05重量%之濃度存在。
可添加硼以增加鋼之硬化度。在合金A之某些實施例中,硼可以0-0.005重量%之濃度存在。在合金B之某些實施例中,硼可以0.0-0.002重量%之濃度存在。
可添加鈦以增加鋼強度、控制沃斯田鐵晶粒尺寸及控制游離氮。在合金B之某些實施例中,鈦可以0.01-0.05重量%之濃度存在;在其他實施例中,鈦可以0.018-0.032重量%之濃度存在;且在其他實施例中,鈦可以0.01-0.025重量%之濃度存在。
加壓硬化鋼可使用習知製鋼、粗加工及精整方法來處理。舉例而言,可各自不斷鑄造合金A及合金B之鋼以製造厚度大約為12-25 cm之板。可隨後將板在1200-1320℃之溫度下再加熱,且熱輥壓成≥ 2.5 mm之最終標準尺寸,其中最終減小道次在大約950℃之溫度下發生。可隨後將鋼在400-675℃之溫度下捲曲。冷卻後,可將鋼卷材在600-900℃之溫度下退火持續長於1秒之時間,且在冷減縮之前酸洗。在達至所需厚度之前可能需要將一或多個中間物退火及減縮之步驟。該中間物退火採用與第一退火處理類似之溫度。
本申請案之合金亦可於冷輥壓後及熱衝壓前經基於鋁之塗層、基於鋅之塗層(鍍鋅或鍍鋅退火中之任一者)塗佈。該塗層可使用此項技術中已知之方法(包括熱浸塗佈或電解塗佈)塗覆於鋼片上。由於臨界溫度較低,本發明合金在其已經塗佈之後的加壓硬化不大可能引起塗層之熔融及與該熔融相關之不利效果。
在本發明之實施例中,將所選合金A及所選合金B之鋼坯料熔接在一起以形成TWB,隨後將其加熱至高於合金A之Ac1之溫度,轉移至模具中,根據標準熱衝壓程序來衝壓及冷卻。在本發明之其他實施例中,將所選合金A及所選合金B之鋼坯料熔接在一起以形成TWB,隨後將其加熱至高於合金A之Ac3之溫度,轉移至模具中,根據標準熱衝壓程序來衝壓及冷卻。可在適當的加壓硬化條件下在合金A中達成大約2,000 MPa之極限抗張強度。在此等相同條件下,合金B之鋼可產生大約700-980 MPa之極限抗張強度及13-20%之總伸長率。
實例1
實例1
三種鋼合金A-1、合金B-1及合金B-2以重量%為單位用以下標稱組合物製備:合金A-1為0.22% C、5% Mn、0.25% Si、0.2% Cr、Fe/雜質-其餘部分;合金B-1為0.09% C、2.3% Mn、0.15% Si、0.02% Ti、Fe/雜質-其餘部分;且合金B-2為0.08% C、1.7% Mn、0.18% Si、0.013% Ti、0.035% V、0.017% Mo、Fe/雜質-其餘部分。合金A-1之Ac1
溫度為大約677℃,且使用膨脹測量法測定。
該等鋼中之各者根據不鏽鋼之標準實踐經熔融、鑄造、熱輥壓及冷輥壓。
將該等鋼中之各者之樣品加熱至示於圖1及2中之金屬峰值溫度,且在水冷卻之模具中淬火之前保持300 s。圖1展示加壓硬化模擬後符合合金A及B之鋼之極限抗張強度。圖2展示加壓硬化模擬後符合合金A及B之鋼之總伸長率。
圖1及2展示與合金A及B之組合物對應之鋼的模擬加壓硬化後之性質。表1概述模擬加壓硬化後之性質。
表1-模擬加壓硬化後合金A及B之機械性質
表1-模擬加壓硬化後合金A及B之機械性質
實例2
特製熔接坯料由熔接至合金B之鋼之合金A之鋼製成,其中合金A及合金B含有闡述於下表2中之組成(其中各合金之組成之其餘部分為Fe及與煉鋼相關之雜質):
表2-合金A及B之化學組成(以重量%為單位)
表2-合金A及B之化學組成(以重量%為單位)
方法A:熔接後,將坯料加熱至高於合金A之Ac1溫度之溫度,轉移至模具中,在模具中成形且隨後冷卻。
方法B:熔接後,將坯料加熱至高於合金A之Ac3溫度之溫度,轉移至模具中,在模具中成形且隨後冷卻。
實例3
如實例2或以下實例中之任一者或更多者之特製熔接坯料之特製熔接坯料,其中合金A中之碳濃度為0.1-0.35重量%,且可替代地為0.22-0.25重量%。
實例4
如實例2至3中之任一或多者或以下實例中之任一者或更多者之特製熔接坯料之特製熔接坯料,其中合金B中之碳濃度為0.08-0.1重量%;可替代地為0.09-0.12重量%,或可替代地為0.06-0.085重量%。
實例5
如實例2至4中之任一或多者或以下實例中之任一者或多者之特製熔接坯料之特製熔接坯料,其中合金A中之錳濃度為2.0-5.0重量%;可替代地為3.0重量%-8.0重量%;或可替代地為3.0重量%-5.0重量%。
實例6
如實例2至5中之任一或多者或以下實例中之任一者或多者之特製熔接坯料之特製熔接坯料,其中合金B中之錳濃度為2.2-2.45重量%;可替代地為1.70-1.95重量%;或可替代地為1.65-1.85重量%。
實例7
如實例2至6中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金A中之矽濃度為0.2-0.3重量%。
實例8
如實例2至7中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B中之矽濃度為0.1-0.2重量%,或可替代地為0.15-0.25重量%。
實例9
如實例2至8中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金A中之鉬濃度為0.0-0.6重量%;可替代地為0.1-2.0重量%;可替代地為0.1-0.6重量%;或可替代地為0.4-0.5重量%。
實例10
如實例2至9中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B中之鉬濃度為0.08-0.15重量%;可替代地為0.12-0.24重量%;可替代地為0.14-0.25重量%。
實例11
如實例2至10中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中鉻濃度為2.0-6.0重量%;可替代地為0.2-6.0重量%;或可替代地為0.2-3.0重量%。
實例12
如實例2至11中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B中之鉻濃度為0.5-0.7重量%,可替代地為0.15-0.35重量%,或可替代地為0-0.1重量%。
實例13
如實例2至12中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中鈮濃度為0.01-0.1重量%;可替代地為0.001-0.055重量%。
實例14
如實例2至13中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B中之鈮濃度為0.03-0.05重量%,可替代地為0.025-0.055重量%,或可替代地為0.0-0.01重量%。
實例15
如實例2至14中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中釩濃度為0.01-0.15重量%。
實例16
如實例2至15中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B中之釩濃度為0.0-0.01重量%,或可替代地為0.02-0.05重量%。
實例17
如實例2至16中之任一或多者或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B中之鈦濃度為0.018-0.032重量%,或可替代地為0.01-0.025重量%。
實例19
如實例2至17或以下實例中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金A用鋁或鋅或其合金塗佈。
實例20
如實例2至19中之一者中之任一或多者之特製熔接坯料之特製熔接坯料,其中合金B用鋁或鋅或其合金塗佈。
圖1展示加壓硬化模擬後符合合金A及合金B之鋼之極限抗張強度。
圖2展示加壓硬化模擬後符合合金A及合金B之鋼之總伸長率。
Claims (21)
- 一種包含合金A及合金B之特製熔接坯料,其中合金A包含0.10-0.50重量% C、0.1-0.5重量% Si、2.0-8.0重量% Mn、0.0-6.0重量% Cr、0.0-2重量% Mo、0.0-0.1重量% Nb、0.0-0.1 Nb及0.0-0.005重量% B,其餘部分為Fe及與煉鋼相關之雜質,且其中合金B包含0.06-0.12重量% C、0.1-0.25重量% Si、1.65-2.45重量% Mn、0.0-0.70重量% Cr、0.08-0.40重量% Mo、0.0-0.1 Nb、0.0-0.05重量% V、0.01-0.05重量% Ti及0.0-0.002重量% B,其餘部分為Fe及與煉鋼相關之雜質。
- 如請求項1之特製熔接坯料,其中合金A中之碳濃度為0.1-0.35重量%。
- 如請求項2之特製熔接坯料,其中合金A中之碳濃度為0.22-0.25重量%。
- 如請求項1之特製熔接坯料,其中合金A中之錳濃度為2.0-5.0重量%。
- 如請求項1之特製熔接坯料,其中合金A中之錳濃度為3.0重量%-8.0重量%。
- 如請求項5之特製熔接坯料,其中合金A中之錳濃度為3.0重量%-5.0重量%。
- 如請求項1之特製熔接坯料,其中合金A中之矽濃度為0.2-0.3重量%。
- 如請求項1之特製熔接坯料,其中合金A中之鉬濃度為0.0-0.6重量%。
- 如請求項1之特製熔接坯料,其中合金A中之鉬濃度為0.1-2.0重量%。
- 如請求項9之特製熔接坯料,其中合金A中之鉬濃度為0.1-0.6重量%。
- 如請求項10之特製熔接坯料,其中合金A中之鉬濃度為0.4-0.5重量%。
- 如請求項1之特製熔接坯料,其中合金A中之鉻濃度為2.0-6.0重量%。
- 如請求項1之特製熔接坯料,其中合金A中之鉻濃度為0.2-6.0重量%。
- 如請求項13之特製熔接坯料,其中合金A中之鉻濃度為0.2-3.0重量%。
- 如請求項1之特製熔接坯料,其中合金A中之鈮濃度為0.01-0.1重量%。
- 如請求項15之特製熔接坯料,其中合金A中之鈮濃度為0.001-0.055重量%。
- 如請求項1之特製熔接坯料,其中釩濃度為0.01-0.15重量%。
- 如請求項1之特製熔接坯料,其中合金A用鋁、鋅或其合金塗佈。
- 如請求項1之特製熔接坯料,其中合金B用鋁、鋅或其合金塗佈。
- 一種製造如請求項1之特製熔接坯料之方法,該方法包含以下步驟: a. 獲得合金A之鋼, b. 獲得合金B之鋼, c. 將該合金A之鋼熔接至該合金B之鋼; d. 將該熔接坯料加熱至高於合金A之Ac1溫度之溫度, e. 在模具中成形, f. 在該模具中冷卻該坯料。
- 一種製造如請求項1之特製熔接坯料之方法,該方法包含以下步驟: a. 獲得合金A之鋼; b. 獲得合金B之鋼; c. 將該合金A之鋼熔接至該合金B之鋼; d. 將該熔接坯料加熱至高於合金A之Ac3溫度之溫度, e. 在模具中成形, f. 在該模具中冷卻該坯料。 [1] K.W. Andrews,Empirical Formulae for the Calculation of Some Transformation Temperatures,JISI,第203卷,1965,第721–727頁。 [2] TRZASKA,J.等人Modelling of CCT Diagrams for Engineering and Constructional Steels .Journal of Materials Processing Technology ,192-193,2007,504-510。 [3] KARIYA,N.High Carbon Hot-Rolled Steel Sheet and Method for Production Thereof . 歐洲專利申請案EP 2.103.697.A1,23.09.2009,15 p。 [4] K.W. Andrews,Empirical Formulae for the Calculation of Some Transformation Temperatures,JISI,第203卷,1965,第721–727頁。
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TW (1) | TW201925495A (zh) |
WO (1) | WO2019090109A1 (zh) |
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CN115305412B (zh) * | 2021-05-05 | 2024-02-06 | 通用汽车环球科技运作有限责任公司 | 具有优异耐腐蚀性和超高强度的组合的压制硬化钢 |
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-
2018
- 2018-11-02 EP EP18836669.4A patent/EP3704281A1/en active Pending
- 2018-11-02 CA CA3076932A patent/CA3076932C/en active Active
- 2018-11-02 MX MX2020004592A patent/MX2020004592A/es unknown
- 2018-11-02 US US16/179,387 patent/US11491581B2/en active Active
- 2018-11-02 WO PCT/US2018/059002 patent/WO2019090109A1/en unknown
- 2018-11-02 TW TW107139065A patent/TW201925495A/zh unknown
Cited By (1)
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CN113996969A (zh) * | 2021-11-10 | 2022-02-01 | 海隆管道工程技术服务有限公司 | 一种高硬度高耐磨管道内壁堆焊药芯焊丝 |
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EP3704281A1 (en) | 2020-09-09 |
MX2020004592A (es) | 2020-08-24 |
US20190126400A1 (en) | 2019-05-02 |
WO2019090109A1 (en) | 2019-05-09 |
US11491581B2 (en) | 2022-11-08 |
CA3076932C (en) | 2023-08-15 |
CA3076932A1 (en) | 2019-05-09 |
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