JP6830493B2 - Warm rolled steel containing rollable austenite - Google Patents
Warm rolled steel containing rollable austenite Download PDFInfo
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- JP6830493B2 JP6830493B2 JP2018536491A JP2018536491A JP6830493B2 JP 6830493 B2 JP6830493 B2 JP 6830493B2 JP 2018536491 A JP2018536491 A JP 2018536491A JP 2018536491 A JP2018536491 A JP 2018536491A JP 6830493 B2 JP6830493 B2 JP 6830493B2
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- 229910000831 Steel Inorganic materials 0.000 title claims description 76
- 239000010959 steel Substances 0.000 title claims description 76
- 229910001566 austenite Inorganic materials 0.000 title description 26
- 238000005096 rolling process Methods 0.000 claims description 54
- 238000005097 cold rolling Methods 0.000 claims description 25
- 238000000034 method Methods 0.000 claims description 21
- 230000008569 process Effects 0.000 claims description 5
- 238000000137 annealing Methods 0.000 claims description 4
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 238000005098 hot rolling Methods 0.000 claims 1
- 229910000734 martensite Inorganic materials 0.000 description 19
- 239000000203 mixture Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 8
- 230000009467 reduction Effects 0.000 description 8
- 230000008901 benefit Effects 0.000 description 6
- 230000009466 transformation Effects 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 4
- 239000002826 coolant Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000010792 warming Methods 0.000 description 3
- 239000011651 chromium Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 230000004580 weight loss Effects 0.000 description 2
- AXDLCFOOGCNDST-VIFPVBQESA-N (2s)-3-(4-hydroxyphenyl)-2-(methylamino)propanoic acid Chemical compound CN[C@H](C(O)=O)CC1=CC=C(O)C=C1 AXDLCFOOGCNDST-VIFPVBQESA-N 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 241000277306 Esocidae Species 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
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- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0231—Warm rolling
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Rolling (AREA)
Description
本出願は、２０１６年１月１４日に圧延可能なオーステナイトを含む温間圧延鋼という発明の名称で出願された米国仮出願第６２／２７８，５６７号、及び２０１６年１０月１２日に圧延可能なオーステナイトを含む温間圧延鋼という発明の名称で出願された米国特許出願第６２／４０７，００１号に対する優先権の利益を主張し、その出願の全内容が本参照により本明細書に組み込まれる。 This application is filed under the name of the invention of warm rolled steel containing austenite that can be rolled on January 14, 2016, US provisional application No. 62 / 278,567, and rollable on October 12, 2016. Claims the benefit of priority over US Patent Application No. 62 / 407,001 filed under the name of the invention of warm rolled steel containing austenite, the entire contents of which are incorporated herein by reference. ..
準安定オーステナイトを含む鋼の冷間圧延は、準安定オーステナイトの高強度マルテンサイト相への変形誘起変態してしまうため、困難であり得る。そのような鋼を冷間圧延すると、圧延負荷が大幅に増加する。鋼はまた、さらなる冷間圧下が行われる前に、部分オーステナイトまたは完全オーステナイトに焼鈍処理する必要がある。
この出願の発明に関連する先行技術文献情報としては、以下のものがある（国際出願日以降国際段階で引用された文献及び他国に国内移行した際に引用された文献を含む）。
（先行技術文献）
（特許文献）
（特許文献１） 特開平０７―０６８５８４号公報
（特許文献２） 米国特許出願公開第２０１２／０７０３３０号明細書
（特許文献３） 米国特許第３，５９９，３２０号明細書
（非特許文献）
（非特許文献１） ＡＮＧＥＬＩＮＥ ＰＯＵＬＯＮ，ＳＴＥＰＨＡＮＩＥ ＢＲＯＣＨＥＴ，ＪＥＡＮ−ＢＥＲＮＡＲＤ ＶＯＧＴ，ＪＥＡＮ−ＣＨＲＩＳＴＯＰＨＥ ＧＬＥＺ，ＪＥＡＮ−ＤＥＮＩＳ ＭＩＴＨＩＥＵＸ： "Ｆｉｎｅ Ｇｒａｉｎｅｄ Ａｕｓｔｅｎｉｔｉｃ Ｓｔａｉｎｌｅｓｓ Ｓｔｅｅｌｓ： Ｔｈｅ Ｒｏｌｅ ｏｆ Ｓｔｒａｉｎ Ｉｎｄｕｃｅｄ ａｌｐｈａ’−Ｍａｒｔｅｎｓｉｔｅ ａｎｄ ｔｈｅ Ｒｅｖｅｒｓｉｏｎ Ｍｅｃｈａｎｉｓｍ Ｌｉｍｉｔａｔｉｏｎｓ"，ＩＳＩＪ ＩＮＴＥＲＮＡＴＩＯＮＡＬ，ｖｏｌ．４９，１ Ｊａｎｕａｒｙ ２００９（２００９−０１−０１），ｐａｇｅｓ ２９３−３０１
（非特許文献２） ＢＯＧＡＣＨＥＶ Ｉ Ｎ； ＥＩＳＭＯＮＤＴ Ｔ Ｄ； ＦＵＧＭＡＮ Ａ Ｖ： "Ｅｆｆｅｃｔ ｏｆ ｗａｒｍ ｒｏｌｌｉｎｇ ｏｎ ｍｅｃｈａｎｉｃａｌ ｐｒｏｐｅｒｔｉｅｓ ｏｆ ｍｅｔａｓｔａｂｌｅ ａｕｓｔｅｎｉｔｉｃ ｃｈｒｏｍｉｕｍ−ｍａｎｇａｎｅｓｅ ｓｔｅｅｌｓ"．ＦＩＺＩＫＡ ＭＥＴＡＬＬＯＶ Ｉ ＭＥＴＡＬＬＯＶＥＤＥＮＩＥ １９７２ ＵＳＳＲ，ｖｏｌ．３４，ｎｏ．５，１ Ｊａｎｕａｒｙ １９７２（１９７２−０１−０１）．ｐａｇｅｓ １０３４−１０４１
（非特許文献３） ＯＬＳＯＮ Ｇ Ｂ； ＡＺＲＩＮ Ｍ： "Ｔｒａｎｓｆｏｒｍａｔｉｏｎ ｂｅｈａｖｉｏｒ ｏｆ ＴＲＩＰ ｓｔｅｅｌｓ"，ＭＥＴＡＬＬＵＲＧＩＣＡＬ ＴＲＡＮＳＡＣＴＩＯＮＳ Ａ（ＰＨＹＳＩＣＡＬ ＭＥＴＡＬＬＵＲＧＹ ＡＮＤ ＭＡＴＥＲＩＡＬＳ ＳＣＩＥＮＣＥ），ｖｏｌ．９Ａ，ｎｏ．５，１ Ｍａｙ １９７８（１９７８−０５−０１），ｐａｇｅｓ ７１３−７２１
（非特許文献４） Ｋｏｈ−Ｉｃｈｉ Ｓｕｇｉｍｏｔｏ ＥＴ ＡＬ："Ｅｆｆｅｃｔｓ ｏｆ Ｖｏｌｕｍｅ Ｆｒａｃｔｉｏｎ ｏｆ Ｒｅｔａｉｎｅｄ Ａｕｓｔｅｎｉｔｅ ｏｎ Ｄｕｃｔｉｌｉｔｙ ａｎｄ Ｓｔａｂｉｌｉｔｙ ｏｆ ＴＲＩＰ−ａｉｄｅｄ Ｄｕａｌ−ｐｈａｓｅ Ｓｔｅｅｌｓ"，ＩＳＩＪ Ｉｎｔｅｒｎａｔｉｏｎａｌ ｖｏｌ．３２，１ Ｊａｎｕａｒｙ １９９２（１９９２−０１−０１），ｐａｇｅｓ １３１１−１３１８
Cold rolling of steel containing metastable austenite can be difficult because it undergoes deformation-induced transformation of the metastable austenite into the high-strength martensite phase. Cold rolling of such steel significantly increases the rolling load. The steel also needs to be annealed to partial or full austenite before further cold reduction is performed.
Prior art document information related to the invention of this application includes the following (including documents cited at the international stage after the international filing date and documents cited when domestically transferred to another country).
(Prior art document)
(Patent document)
(Patent Document 1) Japanese Patent Application Laid-Open No. 07-068584
(Patent Document 2) US Patent Application Publication No. 2012/0703030
(Patent Document 3) US Pat. No. 3,599,320
(Non-patent document)
(Non-Patent Document 1) ANGELINE POULON, STEPHANIE BROCHET, JEAN-BERNARD VOGT, JEAN-CHRISTOPHE GLEZ, JEAN-DENIS MITHIEUX: "Fine Grained Austenitic Stainless Steels: The Role of Strain Induced alpha'-Martensite and the Reversion Mechanism Limitations", ISIJ INTERRNATIONAL, vol. 49,1 January 2009 (2009-01-01), pages 293-301
(Non-Patent Document 2) BOGACHEV IN; EISMONDT T D; FUGMAN AV: "Effective of warm rolling on mechanical products of metastable austenitic chromium" FIZIKA METALLOV I METALLOVEDENIE 1972 USSR, vol. 34, no. 5,1 January 1972 (1972-01-01). pages 1034-1041
(Non-Patent Document 3) OLSON GB; AZRIN M: "Transformation behavior of TRIP steels", METALLURGICAL TRANSACTIONS A (PHYSICAL METALLURGY AND MATERIALS SCENC) 9A, no. 5,1 May 1978 (1978-05-01), pages 713-721
(Non-Patent Document 4) Koh-Ichi Sugimoto ET AL: "Effectives of Volume Fraction of Retained Austenite on Ductility and Stability of TRIP-aided D.I. 32,1 January 1992 (1992-01-01), pages 1311-1318
本発明は、オーステナイトからマルテンサイトへの変態を抑制するために、冷間圧延の前または最中に材料を加温する工程を含む。これは、同様の負荷での圧延機負荷の低下および高い減少量を生じさせ得る。さらに材料を減少させる能力は、材料が最終的なゲージに到達する前に中間焼鈍を少なくすることにもつながる。驚くべきことに、温間圧延鋼は、冷間圧延によって同じ量減少した鋼と比較して、機械的特性が向上したことを示した。その後の焼鈍後の温間圧延は、同じ量で冷間圧延し、その後焼鈍された材料でできたものより優れた機械的特性をもたらした。温間圧延され、続いて室温圧延（冷間圧延）された鋼は、強度と延性の両方の向上を示す。 The present invention includes a step of heating the material before or during cold rolling in order to suppress the transformation of austenite to martensite. This can result in a reduction in rolling mill load and a high amount of reduction under similar loads. In addition, the ability to reduce material also leads to less intermediate annealing before the material reaches the final gauge. Surprisingly, warm-rolled steels showed improved mechanical properties compared to steels that were reduced by the same amount by cold-rolling. Subsequent warm rolling after annealing resulted in better mechanical properties than those made of the same amount of cold rolled and then annealed material. Steels that have been warm-rolled and subsequently room-temperature-rolled (cold-rolled) show improvements in both strength and ductility.
従来、潤滑油として使用される油の温暖に関連した目下のリスクばかりでなく、圧延設備に損傷を与える恐れがあるため、温間圧延は生産環境で回避されてきた。本出願は、温間圧延の利点が、適度な温度で、広範囲にわたる方向性を変更せずに達成できることを示す。 Traditionally, warm rolling has been avoided in production environments because of the current risks associated with warming of oils used as lubricants, as well as the potential for damage to rolling equipment. The present application shows that the advantages of warm rolling can be achieved at moderate temperatures without changing a wide range of directions.
本発明は、「準安定鋼」と称される相当量の準安定オーステナイト（１０％〜１００％オーステナイト）を含む鋼に関する。オーステナイトは、機械的変形によりマルテンサイトに変態すると準安定とみなされる。そのようなマルテンサイトは、変形誘起マルテンサイトと称される。そのような準安定オーステナイトを含む鋼は、炭素鋼またはステンレス鋼であり得る。 The present invention relates to steels containing a significant amount of metastable austenite (10% to 100% austenite) called "metastable steel". Austenite is considered metastable when transformed into martensite by mechanical deformation. Such martensite is referred to as deformation-induced martensite. The steel containing such metastable austenite can be carbon steel or stainless steel.
オーステナイトの安定性を特徴付けるいくつかの方法がある。１つの方法は、その化学組成に基づいてオーステナイトの不安定係数（ＩＦ）を計算することである。この因子は、ＩＦを以下のように定義することが米国特許第３，５９９，３２０号（この開示は参照により本明細書に組み込まれる）に記載されている。 There are several ways to characterize the stability of austenite. One method is to calculate the instability factor (IF) of austenite based on its chemical composition. This factor is described in US Pat. No. 3,599,320, which defines IF as follows (this disclosure is incorporated herein by reference).
ＩＦ＝３７．１９３−５１．２４８（％Ｃ）−０．４６７７（％Ｃｒ）−１．０１７４（％Ｍｎ）−３４．３９６（％Ｎ）−２．５８８４（％Ｎｉ） 式１ IF = 37.193-51.248 (% C) -0.4677 (% Cr) -1.0174 (% Mn) -34.396 (% N) -2.5884 (% Ni) Equation 1
０〜２．９と計算されたＩＦ値を有する鋼は「わずかに準安定」と分類され、２．９より大きいＩＦの鋼は「中程度に準安定」と分類される。本発明の方法は、２．９より大きいＩＦを有する準安定オーステナイト含有鋼に最も顕著にあらわれる。 Steels with an IF value calculated from 0 to 2.9 are classified as "slightly metastable" and steels with an IF greater than 2.9 are classified as "moderately metastable". The method of the present invention appears most prominently in metastable austenite-containing steels with an IF greater than 2.9.
オーステナイトの安定性を特徴付ける別の技術は、Ｍｄ３０温度として知られているものを計算または測定することである。所与の準安定鋼組成物について、Ｍｄ３０温度で０．３の真歪までの変形で、オーステナイトの５０％がマルテンサイトに変態する。所与の準安定鋼組成物について、Ｍｄ温度は、変形の際にマルテンサイトが形成されない温度である。ＭｄおよびＭｄ３０の温度は当該技術分野において周知である。実験に基づく決定に加えて、特定の鋼組成物のＭｄ３０温度は、以下を含む文献に見られ得るいくつかの式の１つによっても計算され得る。
Another technique that characterizes the stability of austenite is to calculate or measure what is known as the
Ｃｏｍｐｏｓｉｔｉｏｎ ａｎｄ Ｇｒａｉｎ−Ｓｉｚｅ Ｄｅｐｅｎｄｅｎｃｉｅｓ ｏｆ Ｓｔｒａｉｎ−Ｉｎｄｕｃｅｄ Ｍａｒｔｅｎｓｉｔｉｃ Ｔｒａｎｓｆｏｒｍａｔｉｏｎ ｉｎ Ｍｅｔａｓｔａｂｌｅ Ａｕｓｔｅｎｉｔｉｃ Ｓｔａｉｎｌｅｓｓ Ｓｔｅｅｌｓ．Ｊｏｕｒｎａｌ ｏｆ Ｉｒｏｎ ａｎｄ Ｓｔｅｅｌ Ｉｎｓｔｉｔｕｔｅ ｏｆ Ｊａｐａｎ，６３（５），ｐｐ．２１２−２２２（その開示内容は本明細書の一部を構成する。）
Ｍｄ３０＝５５１−４６２（％Ｃ＋％Ｎ）−６８＊％Ｃｂ−１３．７＊Ｃｒ−２９（％Ｃｕ＋％Ｎｉ）−８．１＊％Ｍｎ−１８．５＊％Ｍｏ−９．２＊％Ｓｉ 式２
Composition and Grain-Size Dependencyes of Strine-Induced Martensitic Transformation in Metastable Austenitic Stainless Steels. Journal of Iron and Steel Institute of Japan, 63 (5), pp. 212-222 (the disclosure of which constitutes part of this specification).
１９５４年、Ａｎｇｅｌ、Ｔ．によって教示されるＦｏｒｍａｔｉｏｎ ｏｆ Ｍａｒｔｅｎｓｉｔｅ ｉｎ Ａｕｓｔｅｎｉｔｉｃ Ｓｔａｉｎｌｅｓｓ Ｓｔｅｅｌｓ．Ｊｏｕｒｎａｌ ｏｆ ｔｈｅ Ｉｒｏｎ ａｎｄ Ｓｔｅｅｌ Ｉｎｓｔｉｔｕｔｅ，１７７（５），ｐｐ．１６５−１７４（この開示は参照により本明細書に組み込まれる）。
Ｍｄ３０＝４１３−４６２＊（％Ｃ＋％Ｎ）−１３．７＊％Ｃｒ−８．１＊％Ｍｎ−１８．５＊Ｍｏ−９．５＊％Ｎｉ−９．２＊％Ｓｉ 式３
1954, Angel, T. et al. Formation of Martensite in Austenitic Stainless Steels. Journal of the Iron and Steel Institute, 177 (5), pp. 165-174 (this disclosure is incorporated herein by reference).
所与の準安定鋼組成物のオーステナイトのＭｄ３０温度が高いほど、オーステナイトが不安定になる。そのような準安定オーステナイトにおけるＭｄ３０温度は、Ｍｓ温度（熱マルテンサイトのマルテンサイト開始温度）より高い。
The higher the
多量の準安定オーステナイト加工を有する鋼は、オーステナイトがより高強度のマルテンサイトに変態するにつれて急速に硬化する。この加工硬化、及び生じたマルテンサイトは、圧延機の能力を超える可能性がある負荷を必要とし得るため、そのような鋼をさらに冷間圧延する際に課題が生まれる可能性がある。そのような準安定鋼はその後、さらに冷間圧延する前にオーステナイトの一部または全部を形成するために焼鈍される必要がある。圧延中にオーステナイトからマルテンサイトへの変態が抑制されれば、鋼はより低い圧延荷重でより薄いゲージに圧延することができる。そのような変態を抑制する１つの方法は、冷間圧延の前またはその間に材料を温めることである。温間圧延は、より優れた機械的性質をもたらすという付加的な利点を有することを示す。 Steels with large amounts of metastable austenite processing harden rapidly as austenite transforms into higher strength martensite. This work hardening, and the resulting martensite, can require loads that can exceed the capacity of the rolling mill, which can create challenges when further cold rolling such steels. Such metastable steels then need to be annealed to form some or all of the austenite before further cold rolling. If the austenite-to-martensite transformation is suppressed during rolling, the steel can be rolled to thinner gauges with lower rolling loads. One way to suppress such transformations is to warm the material before or during cold rolling. Warm rolling has been shown to have the additional advantage of providing better mechanical properties.
本出願の方法は、鋼を温める間、そのような準安定鋼を転動させる工程を含む。準安定な鋼の温度が室温（一般的に約８０°Ｆ）を上回ると、それは温かいとみなされる。特定の実施形態では、鋼は特定の準安定鋼組成物のＭｄ温度に近いかまたはそれより高い温度に加温される。他の実施形態では、鋼は特定の準安定な鋼組成物のＭｄ３０温度以上の温度に加温される。他の実施形態では、準安定鋼を２５０°Ｆまたはそれ未満の温度に加温される。
The method of the present application comprises rolling such metastable steel while warming the steel. When the temperature of metastable steel exceeds room temperature (generally about 80 ° F), it is considered warm. In certain embodiments, the steel warmed by the or a temperature higher than near M d temperatures of particular metastable steel composition. In other embodiments, the steel is heated to a temperature greater than or equal to the
そのような材料のコイルは、以下の方法のうちの１つまたはそれらの組み合わせを含む、当業者に明らかな方法で加温され得る。 Coil of such material can be heated by methods apparent to those skilled in the art, including one of the following methods or a combination thereof.
Ｉ．コイルを炉／オーブン内で温めてから圧延ライン上に置く。 I. Warm the coil in a furnace / oven before placing it on the rolling line.
ＩＩ．冷間圧延する前に、ヒーターを使用してライン上のコイルを温める。 II. A heater is used to heat the coils on the line before cold rolling.
ＩＩＩ．鋼材を圧延する前に、圧延機上の冷却材を温める。これはいくつかの方法で実行可能である。１つの方法は、圧延機上の冷却塔を止め、準安定鋼を圧延する前に冷却剤を温めるためにいくつかの他の材料を使用する。圧延の前に冷却剤を加温する他の方法は、当業者には明らかであろう。 III. Before rolling the steel, warm the coolant on the rolling mill. This can be done in several ways. One method shuts down the cooling tower on the rolling mill and uses some other material to warm the coolant before rolling the metastable steel. Other methods of warming the coolant prior to rolling will be apparent to those skilled in the art.
準安定鋼は、特定の組成物のための典型的な金属製造処理に従って、冷間圧延（適用可能な場合）前に、溶融、鋳造、熱間圧延、および焼鈍される。準安定鋼の冷間圧延処理中に、少なくとも一回の「冷間圧延」経路は、鋼を温める間、すなわち鋼が８０°Ｆを超える温度で温める間に行われる「温間圧延」経路である。いくつかの実施形態では、鋼は２５０°Ｆ以下の温度に加温される。他の実施形態では、準安定鋼は、特定の準安定鋼組成物のＭｄ温度に近いか、またはそれより高い温度に加温される。他の実施形態では、準安定鋼は、特定の準安定鋼組成物のＭｄ３０温度に近いかまたはそれより高い温度に加温される。このような温間圧延経路は、第一、第二、またはそれに続く「冷間圧延」工程のうちの１つまたは複数であり得る。
Metastable steels are melted, cast, hot rolled, and annealed prior to cold rolling (if applicable) according to typical metalmaking processes for a particular composition. During the cold rolling process of metastable steel, at least one "cold rolling" path is the "warm rolling" path performed while the steel is warmed, that is, while the steel is warmed to a temperature above 80 ° F. is there. In some embodiments, the steel is heated to a temperature below 250 ° F. In another embodiment, the metastable steel, or close to the M d temperature specific metastable steel composition, or be warmed to a higher temperature. In other embodiments, the metastable steel is heated to a temperature close to or higher than the
本発明のいくつかの実施形態では、準安定鋼は１またはそれ以上の温間圧延工程の後に焼鈍されても良い。例えば、「冷間圧延」処理の間、準安定鋼は第一経路で温間圧延され、焼鈍され、次に第二経路で冷間圧延（室温で）されても良い。 In some embodiments of the invention, the metastable steel may be annealed after one or more warm rolling steps. For example, during the "cold rolling" process, the metastable steel may be warm rolled in the first path, annealed, and then cold rolled (at room temperature) in the second path.
実施例１
準安定な鋼は、不安定係数が８．５およびＭｄ３０（Ｎｏｈａｒａ）＝４４７．６°Ｆである化学物質で熱を溶融することによって調製された。熱は連続的にスラブに鋳込まれた。スラブを２３００°Ｆに再加熱し、１０００°Ｆのコイル温度で０．１７５"の厚さまで熱間圧延した。熱帯は、その後、酸化膜を取り除くために酸洗した。酸洗した熱帯の断面を冷間圧延し、温間圧延した。温間圧延の目的のために、熱帯部分を炉内で所望の温度に加温し、所望のゲージに圧延した。
Example 1
Metastable steels were prepared by melting heat with a chemical having an instability factor of 8.5 and M d 30 (Nohara) = 447.6 ° F. The heat was continuously cast into the slab. The slab was reheated to 2300 ° F and hot rolled to a thickness of 0.175 "at a coil temperature of 1000 ° F. The tropics were then pickled to remove the oxide film. A cross section of the pickled tropics. Was cold-rolled and warm-rolled. For the purpose of warm-rolling, the tropical portion was heated to a desired temperature in a furnace and rolled to a desired gauge.
図１は、そのような準安定鋼の冷間圧延及び温間圧延からのマルテンサイト変形の量を示す。同じ減少量では、各温間圧延鋼のマルテンサイト量は、室温で圧延された冷間圧延鋼の場合よりもはるかに少ない。温間圧延の利点は、低温（この実施例では１５０°Ｆ）で見られるが、温間圧延（この実施例では２５０°Ｆ）中の温度が高いほど、形成されるマルテンサイトの量が少なくなる。 FIG. 1 shows the amount of martensitic deformation from cold and warm rolling of such metastable steels. For the same reduction, the amount of martensite in each warm-rolled steel is much less than in cold-rolled steel rolled at room temperature. The advantage of warm rolling is seen at low temperatures (150 ° F in this example), but the higher the temperature during warm rolling (250 ° F in this example), the less martensite is formed. Become.
図２は、温間圧延および冷間圧延後の準安定鋼の異なる伸び量に対する伸長率％を示す。驚くべきことに、温間圧延は、降下を開始する前に一定量の減少まで伸長率％の増加をもたらした。温間圧延の利点は、ある温度で行われる還元の量を変えることによって、または温度を変えることによって調整し得る。一方、室温での冷間圧延は、常に準安定鋼の伸長率％の減少をもたらす。 FIG. 2 shows% of elongation rate for different elongation amounts of metastable steel after warm rolling and cold rolling. Surprisingly, warm rolling resulted in an increase in elongation% up to a certain amount of decrease before the descent began. The advantages of warm rolling can be adjusted by varying the amount of reduction performed at a given temperature or by varying the temperature. On the other hand, cold rolling at room temperature always results in a% reduction in metastable steel elongation.
実施例２
１３．１１及びＭｄ３０（Ｎｏｈａｒａ）＝２２７．６°Ｆの不安定係数を有する化学物質を選択することにより、別の準安定鋼を調製した。熱はインゴットに鋳込まれた。インゴットをトリミングした後、５．７５インチ（Ｗ）×２．７５インチ（Ｔ）×２．７５インチ（Ｌ）の４本の帯を得た。これらのトリミングされたインゴットを２２００°Ｆで浸漬し、１１００°Ｆの仕上げ温度で０．２"まで熱間圧延した。次に熱帯を酸洗して酸化膜を除去した。酸洗した熱帯の断面を冷間圧延し、異なる温度で温間圧延した。温間圧延の目的のために、熱帯部分を炉内の所望の温度に加温し、所望のゲージに圧延した。
Example 2
Another metastable steel was prepared by selecting chemicals with an instability factor of 13.11 and M d 30 (Nohara) = 227.6 ° F. The heat was cast into the ingot. After trimming the ingot, four strips of 5.75 inch (W) x 2.75 inch (T) x 2.75 inch (L) were obtained. These trimmed ingots were dipped at 2200 ° F and hot rolled to 0.2 "at a finishing temperature of 1100 ° F. Then the tropics were pickled to remove the oxide film. The cross section was cold rolled and warm rolled at different temperatures. For the purpose of warm rolling, the tropical part was heated to the desired temperature in the furnace and rolled to the desired gauge.
そのような準安定鋼では、冷間圧延後の温間圧延では、強度と伸長率の両方が増加した。従来の温間圧延なしでは、予想どおり、同じ鋼は強度の増加を示したが、一方で伸長率％の減少を示した。図３（ａ）は、温間圧延３０％後に室温で冷間圧延を施した準安定鋼の真応力歪みデータを示す。図３（ａ）及び（ｂ）において、「ＷＲ」は温間圧延を示し、「ＲＴ」は室温での冷間圧延を示す。３０％の温間圧延に続いてさらに１０％の冷間圧延では、伸長および強度の両方において増加を示した。図３（ｂ）に示すように、３０％冷間圧延した後に０〜３０％の室温で追加の冷間圧延を施した場合、最大抗引張力（ＵＴＳ）は増加したが、予想どおり、伸長率は減少した。また、温間圧延の利点は、ある温度で行われる減少量を変化させることによって、または温度を変化させることによって調整し得ることである。 In such metastable steels, both strength and elongation increased in warm rolling after cold rolling. Without conventional warm rolling, as expected, the same steel showed an increase in strength, while a decrease in elongation%. FIG. 3A shows true stress strain data of a metastable steel subjected to cold rolling at room temperature after 30% of warm rolling. In FIGS. 3A and 3B, "WR" indicates warm rolling and "RT" indicates cold rolling at room temperature. A further 10% cold rolling following a 30% warm rolling showed an increase in both elongation and strength. As shown in FIG. 3 (b), when 30% cold rolling was followed by additional cold rolling at room temperature of 0 to 30%, the maximum tensile strength (UTS) increased, but as expected, elongation. The rate has decreased. Also, the advantage of warm rolling is that it can be adjusted by varying the amount of reduction performed at a certain temperature or by varying the temperature.
実施例３
上記の実施例１の準安定鋼は、以下の表１および２に示す試験データによってさらに示されるように、準安定オーステナイトを含有する鋼上への温間圧延の効果を示し、これは、プラント（コイル２）で２５％温間圧延された準安定オーステナイトを含む鋼と、完全に焼鈍された（コイル１）準安定オーステナイトを含む鋼の特性を比較するものである。
The semi-stable steel of Example 1 above showed the effect of warm rolling onto steel containing semi-stable austenite, as further shown by the test data shown in Tables 1 and 2 below, which is the plant. This is a comparison of the properties of a steel containing semi-stable austenite that has been warm-rolled 25% in (coil 2) and a steel that contains semi-stable austenite that has been completely annealed (coil 1).
実施例４
実施例１の準安定鋼について、異方性に対する温間圧延の効果が研究された。異方性は、その後の成形に著しい影響を及ぼし得る。温間圧延は、準安定鋼の機械的性質における異方性を管理するのに役立つ。
Example 4
For the metastable steel of Example 1, the effect of warm rolling on anisotropy was studied. Anisotropy can have a significant effect on subsequent molding. Warm rolling helps control anisotropy in the mechanical properties of metastable steels.
冷間圧延と比較した温間圧延の効果は、以下の表３に示すデータによってさらに実証される。最初の熱帯は両方のローリングセットで同じだった。１セットは、さまざまな減量（１０、１５および２０％）で温間圧延（＠〜２５０°Ｆ）し、その他は同減量で冷間圧延された。冷間圧延されたサンプルの場合、縦方向（Ｌ）および横方向（Ｔ）の伸長率はかなり異なる。減少量が大きいほど、前記差は大きい。しかし、温間圧延の場合、その差ははるかに小さい。
Claims (5)
ａ．２．９またはそれより大きい不安定係数（ＩＦ）を有する準安定鋼を選択する工程であって、ＩＦは以下の式：
ＩＦ＝３７．１９３−５１．２４８（％Ｃ）−０．４６７７（％Ｃｒ）−１．０１７４（％Ｍｎ）−３４．３９６（％Ｎ）−２．５８８４（％Ｎｉ）
によって計算される、前記選択する工程と、
ｂ．前記準安定鋼を熱間圧延する工程と、
ｃ．前記熱間圧延する工程後および冷間圧延する工程前または間に、６６℃より高く、１２１℃またはそれより低い加温温度に前記準安定鋼を加温する工程と、および
ｄ．第一の圧延する工程において、前記準安定鋼を圧延する工程と、
を有する方法。 A method of rolling metastable steel
a. In the process of selecting a metastable steel having an instability coefficient (IF) of 2.9 or higher, the IF is the following formula:
IF = 37.193-51.248 (% C) -0.4677 (% Cr) -1.0174 (% Mn) -34.396 (% N) -2.5884 (% Ni)
Calculated by the above-mentioned selected steps and
b. The process of hot rolling the metastable steel and
c. A step prior to or during that step and after cold rolling to rolling the hot, higher than 66 ° C., the step of heating said metastable steel lower than 121 ° C. or elevated temperatures, and
d . In the first rolling step, the step of rolling the metastable steel and
Method to have.
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| US62/407,001 | 2016-10-12 | ||
| PCT/US2017/013717 WO2017124081A1 (en) | 2016-01-14 | 2017-01-17 | Warm rolling of steels containing metastable austenite |
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