TW201726942A - 熱加工工具鋼 - Google Patents
熱加工工具鋼 Download PDFInfo
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Abstract
本發明關於熱加工工具鋼。鋼包括以下主要成分(重量%):C 0.27~0.38,Si 0.10~0.35,Mn 0.2~0.7,Cr 4.5~5.5,Mo 2.05~2.90,V 0.4~0.6,N 0.01~0.12,H □0.0004,S □0.0015,其餘為可選用的元素、鐵和雜質。
Description
本發明關於熱加工工具鋼。
釩合金化的基質工具鋼已經在市場上數十年,並且引起極大的興趣,因為它們結合了高抗磨耗性和優異的尺寸穩定性,以及因為它們具有良好的韌性。這些鋼具有廣泛的應用,例如用於模具鑄造和鍛造。鋼的生產一般而言是以習用的冶金,接著再做電熔渣重熔(electro slag remelting,ESR)。
雖然ESR所生產之釩合金化的基質工具鋼就熱裂,大龜裂、熱磨耗、塑性變形來說具有優於傳統生產之工具鋼的性質,但是需要進一步改良以便減少熱加工工具失效的風險,例如在高壓模具鑄造中的熱裂和大龜裂。附帶而言,進一步改善熱加工工具鋼的熱強度和抗回火性則會是有利的。
本發明的目的是提供熱加工工具鋼,其具有改善的性質概況而導致增加工具的壽命。
本發明的另一目的是改善熱裂,同時仍維持良好的抗熱磨耗性和良好的抗大龜裂性。又另一個目的是提供一種鋼組成物,其呈粉末形
式時係適合加成性製造(Additive Manufacturing,AM),尤其適合製作或修復射出成形工具和模具。
藉由提供具有如合金請求項所列組成的熱加工工具鋼,而顯著程度地達到了前面的目的以及額外的優點。
本發明界定於申請專利範圍中。
以下簡短解釋個別元素的重要性和其彼此的交互作用以及所請合金的化學成分限制。全篇鋼的所有化學組成百分比都是重量%(wt.%)。堅硬相的份量是以體積%(vol.%)來表示。個別元素的上下限可以在申請專利範圍所列的限制裡自由組合。
碳要出現的最小含量是0.27%,較佳而言至少0.28、0.29、0.30、0.31、0.32、0.33或0.34%。碳的上限是0.38%,並且可以設為0.37、0.36或0.35%。較佳的範圍是0.30~0.38%和0.33~0.37%。於任何情況,碳的份量應控制成使得鋼中M23C6、M7C3、M6C等類型之初生碳化物的份量受到限制;較佳而言,鋼沒有此等初生碳化物。
矽用來去氧化。Si在鋼中呈溶解形式。Si是強的肥粒鐵形成劑,並且增加碳活性,因此增加形成不想要之碳化物的風險,這負面影響了衝擊強度。矽也易於在介面偏析,這可以導致韌性和抗熱疲勞性減低。
Si因此限於0.35%。上限可以是0.34、0.32、0.31、0.30、0.29、0.28、0.27、0.26、0.25、0.24、0.23、0.22%。下限可以是0.12、0.14、0.16、0.18、0.20%。較佳的範圍是0.10~0.25%和0.15~0.24%。
錳有助於改善鋼的硬化性,並且錳連同硫藉由形成硫化錳而有助於改善車削性。錳因此將出現0.2%的最小含量。下限可以設為0.25、0.3、0.35、0.4、0.45或0.5%。在較高的硫含量下,錳避免鋼中的紅脆。鋼將包含最大0.7%的Mn。上限可以設為0.65、0.6、0.55或0.5%。
鉻要出現的含量是至少4.0%,以便在熱處理期間、在較大的截面中提供良好的硬化性。如果鉻含量太高,則這可以導致形成高溫肥粒鐵,其減少熱加工性。下限可以是4.6、4.7、4.8或4.9%。上限可以是5.4、5.3、5.2或5.1%。
已知Mo對於硬化性具有極好的效果。鉬對於達到良好二次硬化回應為至關重要的。最小含量是2.05%,並且可以設為2.1、2.15、2.2、2.25或2.3%。鉬是強的碳化物形成元素,也是強的肥粒鐵形成劑。鉬的最大含量因此是2.9%。較佳而言,Mo乃限於2.8、2.7、2.6、2.5、2.4或2.35%。
釩在鋼的基質中形成V(N,C)型之均勻分布的初生析出碳化物和碳氮化物。這堅硬相也可以表示成MX,其中M主要是V,但可以出現Cr和Mo,並且X是C、N、B中的一或多者。釩因此將出現的份量是
0.4~0.6%。上限可以設為0.59、0.58、0.57、0.56或0.55%。下限可以是0.42、0.43、0.44、0.45、0.46、0.47、0.48、0.49、0.50、0.51或0.52%。
本發明人已經發現在室溫和在高溫的拉伸強度受到鋼中碳化物形成元素釩對碳含量之比例的影響。理由相信是關聯於以下事實:這些性質同時取決於碳在基質中的溶解含量以及析出的碳。而且,韌性也受到該比例的影響。基於這些原因,較佳的是比例為1.35~1.65,較佳而言為1.40~1.60,或者更佳而言是1.45~1.55。
如果想要有更顯著的二次硬化,則可以增加釩的總份量,以便補償某些或所有被束縛成更穩定的氮化物的釩。基於這些理由,較佳的是比例為1.55~1.90。它可以設為1.60~1.85或者更佳的是1.65~1.80。
鋁是用來與Si和Mn組合而去氧化。下限設為0.001、0.003、0.005或0.007%以便確保有良好的去氧化。上限則限制為0.06%以便免析出不想要的相,例如AlN。上限可以是0.05、0.04、0.03、0.02或0.015%。
氮乃限制為0.010~0.12%以便獲得想要類型和份量的堅硬相,尤其是V(C,N)。當氮含量與釩含量做適當平衡時,將形成富含釩的碳氮化物V(C,N)。這些將在沃斯田化步驟期間部分溶解,然後在回火步驟期間析出成奈米尺寸的晶粒。碳氮化釩的熱穩定性乃視為優於碳化釩,因此可以改善工具鋼的抗回火性,並且提升在高沃斯田化溫度下的抗晶粒成長
性。下限可以是0.011、0.012、0.013、0.014、0.015、0.016、0.017、0.018、0.019或0.02%。上限可以是0.11、0.10、0.09、0.08、0.07、0.06、0.05、0.04或0.03%。
已知氫對於鋼的性質具有傷害的效果,並且在處理期間引起問題。為了避免有關氫的問題,熔融鋼接受真空除氣。上限是0.0004%(4ppm)並且可以限於3、2.5、2、1.5或1ppm。
鎳可以出現的份量是1.5%。它賦予鋼良好的硬化性和韌性。然而,因為費用的緣故,所以鋼的鎳含量應受到限制。上限可以因此設為1.0、0.8、0.5或0.3%。然而,正常而言不故意添加Ni。
Cu是可選用的元素,其可以幫助增加鋼的硬度和抗腐蝕性。如果使用的話,較佳的範圍是0.02~1%。然而,一旦已經添加了銅就不可能從鋼萃取出銅。這大大的使廢料處理更加困難。為此原因,正常而言不故意添加銅。
Co是可選用的元素。Co使固相線溫度增加,因此提供提升硬化度的機會,其可以比沒有Co時高出15~30℃。在沃斯田化期間,因此有可能溶解較大比例的碳化物以及藉此提升硬化性。Co也增加Ms溫度。然而,大量的Co可以導致韌性和抗磨耗性減少。最大份量是8%;如果添加的話,有效份量可以是2~6%,尤其是4到5%。然而,基於實務原因,例
如廢料處理,不故意添加Co。最大雜質含量則可以設為1%、0.5%、0.3%、0.2%或0.1%。
原則上,鉬可以由二倍的鎢所取代,因為它們在化學上類似。然而,鎢是昂貴的,並且它也使廢金屬的處理變得複雜。最大份量因此限於0.5%,較佳而言為0.3%,並且更佳而言不故意添加。
鈮類似於釩在於它形成M(N,C)型的碳氮化物,並且原則上可以用於取代部分的釩,但相較於釩則需要二倍份量的鈮。然而,Nb導致M(N,C)有更尖角的形狀。最大份量因此是0.5%,較佳而言為0.05%,並且最佳而言不故意添加。
這些元素是碳化物形成劑,並且可以在所請範圍而出現於合金中用於改變堅硬相的組成。然而,正常來說都不添加這些元素。
可以使用B以便進一步增加鋼的硬度。份量乃限於0.01%,較佳而言0.005%。添加B的較佳範圍是0.001~0.004%。
這些元素可以用所請份量來添加到鋼中以修飾非金屬夾雜物以及/或者以便進一步改善車削性、熱加工性和/或焊接性。
P、S、O是主要雜質,其對鋼的機械性質具有負面效果。P
因此可以限於0.03%,較佳而言為0.01%。S乃限於0.0015,並且可以限於0.0012、0.0010、0.0008或0.0005%。O可以限於0.0015、0.0012、0.0010、0.0008、0.0006或0.0005%。
具有所請化學組成的工具鋼可以藉由習用的冶金而生產,包括在電弧爐(electric arc furnace,EAF)中熔解並且在澆桶和真空處理中進一步精煉。可選用而言,鋼可以接受電熔渣重熔(ESR)以便進一步改善潔淨度和微結構均質性。
正常而言,鋼在使用前先接受硬化和回火。沃斯田化可以在範圍是1000~1070℃的沃斯田化溫度(TA)下進行,較佳而言為1030~1050℃。典型的TA是1040℃維持30分鐘,接著快速焠火。回火溫度是根據硬度要求來選擇,並且在600~650℃下2小時進行至少二次(2×2小時),接著在空氣中冷卻。
在本實施例中,藉由EAF熔解、澆桶精煉和真空除氣(vacuum degassing,VD)而生產具有以下組成的鋼(重量%):C 0.35,Si 0.18,Mn 0.47,Cr 5.05,Mo 2.34,V 0.54,
Al 0.009,P 0.005,S 0.0003,H 0.00005,N 0.0051,O 0.0006,V/C 1.54,其餘為鐵和雜質。
在真空除氣之後,鋼藉由核心線射出而接受氮合金化。在該修整之後的最終氮含量是0.0142重量%。
鋼鑄成錠並且接受熱加工。
鋼在1040℃下30分鐘以沃斯田化,並且藉由在600℃、2小時做氣體焠火和回火二次(2×2小時)而硬化,接著在空氣中冷卻。
使用Thermo-Calc來計算氮合金化在三個不同沃斯田化溫度下對於基質組成和初生MX份量的效果。結果顯示於表1。
表1顯露出:在所有三個溫度,未溶解之堅硬相(MX)在氮合金化鋼中的份量顯著高於在未合金化鋼中的份量。MX相負責將晶界釘住,藉此阻礙晶粒生長。據此,本發明的氮合金化在硬化溫度下較不易於發生晶粒成長。這也由實驗所證實,其顯示低氮含量之鋼的晶粒尺寸在1060℃有明顯增加,而對超過1080℃的溫度氮合金化的鋼穩定的對抗晶粒成長。據此,較高的硬化溫度可以用於氮合金化的鋼而不傷害晶粒成長。藉此則有可能影響模具材料中的性質平衡,以便減少熱裂和/或大龜裂的傾向,以及藉此延長模具壽命。
合金在感應爐中熔化並且接受氮氣(5N)霧化。
C 0.34,
Si 0.16,Mn 0.44,Cr 5.01,Mo 2.33,V 0.53,Al 0.008,N 0.044,O 0.0024,V/C 1.59,其餘為鐵和雜質。
粉末過篩到<500微米,並填充於直徑63毫米、高度150毫米的鋼囊中。在1150℃的溫度下進行熱均壓(HIP),維持時間是2小時、壓力為110百萬帕(MPa)。冷卻速率為每秒<1℃。如此獲得的材料則在1130℃下鍛造成20×30毫米的尺寸。在900℃進行軟退火,而冷卻速率為每小時10℃降到750℃,之後在空氣中自由冷卻。未溶解之MX的份量高於前一實施例,並且氮含量比較高。由於此事實以及精細分布了富含氮之碳氮化釩(MX)的緣故,發現鋼對於對抗晶粒成長是極為穩健的。
組成相同於實施例2的粉末接受過篩,以便獲得範圍為10~60微米之窄晶粒尺寸分布的粉末。發現粉末或可成功的用於模具的雷射包覆修復,以及用於譬如具有保形冷卻通道之模具的快速原型設計。據此,鋼合金粉末顯得會適合加成性製造。
本發明的工具鋼可用於需要良好硬化性和良好之抗熱裂和大龜裂性的大模具。合金的霧化粉末可以用於生產具有優異結構均勻性的HIP產品。合金的粉末可以用來生產或修復模具,尤其藉由加成性製造方法來為之。
Claims (10)
- 一種用於熱加工的鋼,其以重量%(wt%)計由以下各者所組成:C 0.27~0.38,Si 0.10~0.35,Mn 0.2~0.7,Cr 4.5~5.5,Mo 2.05~2.90,V 0.4~0.6,N 0.01~0.12,H 0.0004,S 0.0015,可選用而言以下一或多者:Al 0.001~0.06,Ni 1.5,Cu 2,Co 8,W 0.5,Nb 0.5,Ti 0.05,Zr 0.05,Ta 0.05,B 0.01, Ca 0.00005~0.009,Mg 0.01,稀土金屬(REM) 0.2,其餘為Fe以及雜質。
- 根據申請專利範圍第1項的鋼,其滿足以下至少一要求:C 0.30~0.38,Si 0.15~0.30,Mn 0.4~0.6,Cr 4.6~5.4,Mo 2.1~2.8,V 0.5~0.6,N 0.011~0.08,H 0.0003,Cu 0.02~1,Co1,W 0.3,Nb 0.05,Ti 0.01,Zr 0.01,Ta 0.01,B 0.005,Se 0.03, Mg 0.001,Ca 0.00001~0.009,V/C 1.35~1.65,並且其中P、S、O的雜質含量滿足以下要求:P 0.03,S 0.0010,O 0.0015。
- 根據申請專利範圍第1或2項的鋼,其滿足以下至少一要求:C 0.33~0.38,Si 0.15~0.29,N 0.012~0.07,H 0.0002,Cu 0.02~0.5,Co 0.3,W 0.1,B 0.001~0.004,Mg 0.00005~0.001,Ca 0.0001~0.009,V/C 1.40~1.60。
- 根據前面申請專利範圍任一項的鋼,其滿足以下至少一要求:C 0.33~0.37,Si 0.16~0.26, Mn 0.45~0.55,Cr 4.8~5.2,Mo 2.2~2.6,V 0.51~0.58,N 0.011~0.056,H 0.0003,Cu 0.02~0.3,Co 0.3,W 0.1,Nb 0.05,Mg 0.0001~0.001,Ca 0.0001~0.001,V/C 1.45~1.55,P 0.01,S 0.0005,O 0.0008,V+8.8(N-0.005)/C 1.55~1.9。
- 根據前面申請專利範圍任一項的鋼,其中初生析出MX的含量是0.2~3體積%,較佳而言為0.3~1.0體積%。
- 根據申請專利範圍第1~3或5項中任一項的鋼,其滿足以下要求:C 0.30~0.38,Si 0.15~0.30, Mn 0.4~0.6,Cr 4.5~5.5,Mo 2.1~2.8,V 0.5~0.6,N 0.01~0.08,H 0.0003。
- 根據申請專利範圍第1~3、5或6項中任一項的鋼,其滿足以下要求:C 0.33~0.37,Si 0.16~0.26,Mn 0.45~0.55,Cr 4.8~5.2,Mo 2.2~2.6,V 0.51~0.58,N 0.011~0.07。
- 根據前面申請專利範圍任一項的鋼,其中該基質包括回火的麻田散鐵和/或變韌鐵,並且維持之沃斯田鐵的份量乃限於6體積%、5體積%、4體積%或2體積%。
- 根據前面申請專利範圍任一項的鋼,其中以呈粉末的形式提供該鋼,較佳而言其尺寸分布的範圍是5~150微米,更佳而言的範圍是10~100微米或10~60微米,其中該粉末顆粒之平均尺寸的較佳範圍是25~50微米。
- 一種根據申請專利範圍第9項之鋼粉末的用途,其係用於加成性製造,尤其用於製作或修復射出成形工具。
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CN103834869A (zh) | 2012-11-22 | 2014-06-04 | 应振强 | 一种新型5Cr3MnSiMo1VBN耐冲击工具钢 |
JP2017507251A (ja) * | 2014-01-27 | 2017-03-16 | ロバルマ, ソシエダッド アノニマRovalma, S.A. | 鉄系合金の遠心噴霧法 |
JP6366326B2 (ja) | 2014-03-31 | 2018-08-01 | 山陽特殊製鋼株式会社 | 高靱性熱間工具鋼およびその製造方法 |
JP6647771B2 (ja) | 2014-05-23 | 2020-02-14 | 大同特殊鋼株式会社 | 金型用鋼及び金型 |
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2015
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- 2016-11-28 CA CA3009044A patent/CA3009044A1/en active Pending
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- 2016-11-28 CN CN201680075284.8A patent/CN108474085B/zh active Active
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CN108474085A (zh) | 2018-08-31 |
US20190003021A1 (en) | 2019-01-03 |
EP3394309A4 (en) | 2019-01-02 |
CN108474085B (zh) | 2021-08-17 |
WO2017111680A1 (en) | 2017-06-29 |
JP7045315B2 (ja) | 2022-03-31 |
JP2019504197A (ja) | 2019-02-14 |
SE539646C2 (en) | 2017-10-24 |
MX2018007563A (es) | 2018-09-21 |
SI3394309T1 (sl) | 2021-09-30 |
SE1551702A1 (en) | 2017-06-23 |
EP3394309A1 (en) | 2018-10-31 |
RU2018126761A (ru) | 2020-01-28 |
TWI703223B (zh) | 2020-09-01 |
US11131012B2 (en) | 2021-09-28 |
KR20190034491A (ko) | 2019-04-02 |
BR112018012850B1 (pt) | 2022-03-03 |
KR102435470B1 (ko) | 2022-08-23 |
RU2728149C2 (ru) | 2020-07-28 |
BR112018012850A2 (pt) | 2018-12-04 |
CA3009044A1 (en) | 2017-06-29 |
ES2878268T3 (es) | 2021-11-18 |
RU2018126761A3 (zh) | 2020-02-17 |
EP3394309B1 (en) | 2021-05-05 |
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