EP0352597A1 - Procédé de fabrication de feuillard laminé à chaud ou tôles fortes - Google Patents

Procédé de fabrication de feuillard laminé à chaud ou tôles fortes Download PDF

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Publication number
EP0352597A1
EP0352597A1 EP89113109A EP89113109A EP0352597A1 EP 0352597 A1 EP0352597 A1 EP 0352597A1 EP 89113109 A EP89113109 A EP 89113109A EP 89113109 A EP89113109 A EP 89113109A EP 0352597 A1 EP0352597 A1 EP 0352597A1
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EP
European Patent Office
Prior art keywords
max
product
deformation
slab
heat
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP89113109A
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German (de)
English (en)
Other versions
EP0352597B1 (fr
Inventor
Hans Dipl.-Ing. Dr. Pircher
Rudolf Dipl.-Ing. Kawalla
Jürgen Dipl.-Ing. Mahn
Walter Dipl.-Ing. Wilms
Waldemar Dipl.-Ing. Wolpert
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Thyssen Stahl AG
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Thyssen Stahl AG
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Publication date
Application filed by Thyssen Stahl AG filed Critical Thyssen Stahl AG
Publication of EP0352597A1 publication Critical patent/EP0352597A1/fr
Application granted granted Critical
Publication of EP0352597B1 publication Critical patent/EP0352597B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B2201/00—Special rolling modes
    • B21B2201/02—Austenitic rolling

Definitions

  • the invention relates to a method for producing hot strip or heavy plates from rustproof and heat-resistant steels or from wrought alloys based on nickel with a final thickness in the range from 5 to 60 mm by producing a slab from ingot casting or by continuous casting, heating the slab at a temperature above of 1,100 ° C, subsequent hot rolling of the slab and accelerated cooling of the product rolled to its final thickness.
  • a method according to the preamble of claim 1 for the production of austenitic stainless steel plates with high corrosion resistance and high mechanical strength both at ambient temperature and at high temperatures is known from DE-OS 36 17 907. It can be seen from this prior art document that the steel plates, i.e. Heavy plates made of rust-proof austenitic steels of the composition specified in the publication after the roughing and finishing rolling and the subsequent cooling in air to room temperature usually have to be subjected to a subsequent heat treatment or solution annealing. This is carried out so that the hardening caused by the deformation is broken down and precipitations of intermetallic or carbidic phases are dissolved, which negatively affect the corrosion resistance of the product.
  • the subsequent solution annealing must generally take place at temperatures of more than 1,000 ° C. and correspondingly long holding times, which are sufficient to bring the precipitates back into solution.
  • the deformation-related solidification is reduced as a result of recovery and recrystallization.
  • the stainless steel plates or heavy plates produced by this conventional method have in the solution-annealed state with regard to their mechanical properties, e.g. Strength and toughness, as well as corrosion resistance, a property profile that is characterized by low mechanical strength.
  • the object of the patent application described and claimed in DE-OS 36 17 907 is to create a process for producing austenitic stainless steel plates which have better corrosion resistance and tensile strength both at ambient temperatures and at higher temperatures, without the need to use a downstream heating furnace as is required in the conventional process for subsequent solution annealing.
  • the product produced by this process has a much better mechanical and comparable corrosion resistance.
  • a higher strength is achieved in particular if hot rolling is also carried out in the non-recrystallization area.
  • the heating and heating temperature for the slab is preferably in the range from 1,100 to 1,200 ° C.
  • the finish-rolling temperature is in the range from 900 to 970 ° C, that is in any case less than 1,000 ° C and immediately after finish rolling with a temperature loss of only about 10 ° C the accelerated cooling begins, to a value of 500 ° C, preferably 300 ° C, in particular down to room temperature. Only when the final thickness of the product or heavy plate is 40 mm, in particular 100 mm, does a finish rolling temperature of more than 1,000 ° C result.
  • the finish-rolling temperature drops so much that a property profile comparable to that of heavy plates in solution-annealed condition, for example in terms of strength, toughness and corrosion resistance, cannot be set. Rather, the method known from DE-OS 36 17 907 basically gives a higher mechanical strength. However, if this is not desired with regard to the processing and use properties of the heavy plates, the finished rolled plates must then be subjected to a subsequent solution treatment, provided that they have a final thickness of less than 60 mm, in particular less than 40 mm.
  • hot strip and the heavy plates should have a property profile as in the solution-annealed state, then heat treatment or solution annealing is still essential to break down the deformation-related hardening and to dissolve excretions.
  • hot strip and heavy plate with a final thickness of less than 60 mm are primarily affected, in particular those with a thickness in the range between 8 and 40 mm. Accordingly, if an increase in the strength properties is not desired, then with the method known from DE-OS 36 17 907 only heavy plates can be safely produced without subsequent solution treatment, which have a final thickness of more than 60 mm, but are rarely used in practice .
  • so far only the production of hot strip with a final thickness of less than about 8 or 10 mm has been possible without problems, which, however, has to be solution annealed in any case after the finish rolling.
  • EP-OS 0 144 694 discloses a modified process for the production of flat, band-shaped or plate-shaped semifinished products, for example with a final cross section of 15 mm ⁇ 40 mm, from a stainless austenitic or martensitic steel, which, however, provides for solution annealing.
  • the workpiece is first heated from the stainless steel with the composition specified in the publication to a high temperature of the order of 1200 ° C. and heated through at this temperature. It is then pre-rolled and finish-rolled warm at a temperature in the range of 1,000 to 1,100 ° C in such a way that complete recrystallization of the rolling stock is ensured by sufficient deformation during the rolling process.
  • solution annealing and subsequent quenching of the semi-finished product in water take place from this temperature range to almost room temperature.
  • An essential feature of this process is that the solution annealing immediately following the rolling process is carried out in a heat after the last or the last rolling passes and the workpiece is then quenched directly from the solution annealing temperature in water without any additional treatment.
  • this method provides for a roller heating system, which is intended to largely prevent premature and excessive cooling of the workpiece during rolling in order to prevent the finished workpiece from being reheated to the required solution solution and quenching temperature of more than 1,000 ° C.
  • this additional heating for the reheating of the finished rolled product and in particular the proposed roller heating would mean a considerable additional outlay in the production of hot strip or heavy plates, which was previously customary.
  • the invention has for its object to provide a method of the type mentioned, according to which products in the form of hot strip or heavy plates with the composition given in Table 1 are hot-rolled and have a property profile after accelerated cooling, for example with regard to strength, toughness and corrosion resistance , which corresponds to that of solution annealed hot strip or heavy plate.
  • slabs are produced from ingot casting or by continuous casting from rustproof and heat-resistant steels or from wrought alloys based on nickel with the composition given in Table 1 and heated through before the hot rolling at a temperature of more than 1,100 ° C.
  • the hot-rolling of the heated slabs begins without interruption to a maximum of 1/6 of their initial thickness, ie they are reduced to a maximum of 1/6 of their initial thickness with the shortest possible break times between the individual deformation stitches in extreme cases.
  • Hot rolling is predominantly carried out with deformation stitches in which the degree of deformation per stitch in the direction of thickness is greater than the degrees of deformation indicated by curve A in FIG.
  • the initial thickness of the slab or slabs is usually in the order of about 150 to 250 mm. If, however, the slabs produced by continuous casting only have a thickness of the order of about 50 mm or less, the reduction in the product in them can also be used according to the invention the first rolling phase. Usually, however, a pre-rolling phase is followed by finish rolling to the final thickness, which according to measure ac) in claim 1 takes place above a minimum temperature which is dependent on the molybdenum content of the product and which must not be undercut.
  • the accelerated cooling takes place no later than 100 s thereafter at a core speed of more than 3 K / s, preferably more than 5 K / s, except for a temperature equal to or less than 650 ° C.
  • hot strip and heavy plates made of the steels specified in Table 1 can have one end thickness in the range of 5 to 60 mm and with a property profile that corresponds to the mechanical properties and the corrosion resistance of solution-annealed hot strips and heavy plates.
  • the strips and sheets produced according to the invention have a more uniform, in particular very fine-grained and largely excretion-free structure, as a result of which their processing and use properties are improved.
  • thin strips and sheets with a preferred final thickness in the range from 8 to 40 mm can now be hot-rolled to the final thickness without additional heat input during the rolling out in such a way that subsequent solution annealing is no longer required .
  • the properties of the strips and sheets produced by the process according to the invention can be further improved and optimized by hot-rolling and the subsequent accelerated cooling in accordance with the measures specified in subclaims 2 to 7.
  • the method according to claim 3 relates to the production of hot strip and the method according to claim 4 to the production of heavy plates. If at the same time all the deformation stitches of the roughing phase have a degree of deformation which is greater than the degrees of deformation indicated by curve A in FIG. 1, hot strip and heavy plates can be e.g. Manufacture with optimal values in terms of strength, toughness and corrosion resistance.
  • the method according to the invention can preferably be applied to the production of hot strip and heavy plates from rustproof and heat-resistant steels with an analysis according to claims 8 to 11 and 14 to 17 and from a wrought nickel base alloy with the composition specified in claims 12 and 13. If the method is preferably applied to rustproof and heat-resistant austenitic steels with the composition according to claims 16 and 17, hot strip and / or heavy plates with high toughness and increased corrosion resistance are obtained, which afterwards as a finished product are easy to process with regard to hot forming, cold forming and welding have.
  • Table 1 shows the composition of those stainless and heat-resistant steels and wrought alloys based on nickel, from which hot strip and heavy plates can be produced by the process according to the invention.
  • the five different alloys specified in Table 3 were selected, from which hot strip with a final thickness of 10 and 15 mm and heavy plates with a final thickness in the range from 10 to 40 mm were produced by the process according to the invention.
  • These are two stainless austenitic steels with a molybdenum content of less than 1.0%, two further stainless austenitic steels with a molybdenum content of more than 1.0% and a nickel-based alloy with the composition given in Table 3.
  • preliminary slabs with a thickness in the range of 170 to 265 mm were first produced and then heated to a temperature of more than 1,100 ° C. and heated through at this temperature.
  • the hot strip and the heavy plates were then heated from them
  • the slabs were first rolled out to a final thickness in a roughing phase and in a subsequent finishing rolling phase, before the finished rolled product was accelerated to a temperature of less than 650 ° C. at a rate of more than 3 K / s.
  • the degrees of deformation per pass were selected both in the roughing phase and in the finish-rolling phase according to the dependence of the degree of deformation, according to the invention, shown in Table 2 and shown in FIG.
  • Table 4 the hot rolling and cooling conditions, according to which the five different alloys given in Table 3 to form hot strip (W) and heavy plates were rolled out to final thickness, are given in Table 4.
  • the corresponding conditions of hot strip and heavy plate not produced according to the invention are also given.
  • Table 5 compares the results obtained with hot rolled strip and heavy plate produced according to the invention, with solution annealed and not annealed and with solution annealing.
  • Hot rolling in the recrystallization area and at high temperatures is not sufficient to set the properties desired for the hot strip and the heavy plates.
  • a homogeneous and fine-grained structure which is improved compared to the solution-annealed condition can be set provided the hot rolling conditions in the finish rolling phase for hot strip according to subclaims 2 and 3 and for heavy plates according to subclaims 2 and 4 can be set.
  • the hot rolling conditions in the finish rolling phase in addition to measure ac), only the feature ab) according to claim 1, a generally fine-grained structure is also generally achieved, but to a small extent also has coarse grain.
  • the hot strips and heavy plates produced according to the invention have comparable mechanical properties and corrosion resistance to the products in the solution-annealed state.
  • the exemplary embodiments according to the invention and the comparative examples in Tables 4 and 5 show that hot strip and heavy plates made of rustproof and heat-resistant steels or of wrought alloys based on nickel with the composition given in Table 1 with a final thickness in the range from 5 to 60 mm, preferably in the range from 8 to 40 mm, can be produced by the process according to the invention with a property profile which corresponds to the property profile of the corresponding strips and sheets in the solution-annealed state.
  • the strips and sheets produced according to the invention advantageously have a homogeneous and fine-grained structure that is largely free of excretions, which further improves their processing and use properties.
  • the method according to the invention now makes it possible, in particular, to produce hot strip with a final thickness greater than approximately 5 mm in a simple and inexpensive manner by controlled hot rolling with subsequent accelerated cooling without the need for subsequent solution annealing.
  • Table 1 Stainless and heat-resistant steels Wrought alloys based on Ni ferritic and martensitic austenitic / ferritic austenitic Alloy element Alloy content in mass% carbon ⁇ 0.35 ⁇ 0.05 ⁇ 0.15 ⁇ 0.1 manganese ⁇ 2.5 ⁇ 10.0 ⁇ 20.0 ⁇ 4.0 silicon ⁇ 1.5 ⁇ 1.5 ⁇ 4.0 ⁇ 4.0 nickel ⁇ 3.0 4 - 7 ⁇ 35 (Rest Ni) chrome 6 - 30.0 10 - 30.0 10 - 30.0 10 - 30 molybdenum ⁇ 3.0 ⁇ 5.0 ⁇ 7.0 ⁇ 10 titanium ⁇ 1.5 ⁇ 1.5 ⁇ 1.5 Tantalum and / or niobium ⁇ 1.5 ⁇ 1.5 ⁇ 1.5 ⁇ 1.5 copper copper

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP89113109A 1988-07-28 1989-07-18 Procédé de fabrication de feuillard laminé à chaud ou tôles fortes Expired - Lifetime EP0352597B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE3825634A DE3825634C2 (de) 1988-07-28 1988-07-28 Verfahren zur Erzeugung von Warmbad oder Grobblechen
DE3825634 1988-07-28

Publications (2)

Publication Number Publication Date
EP0352597A1 true EP0352597A1 (fr) 1990-01-31
EP0352597B1 EP0352597B1 (fr) 1994-06-22

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EP89113109A Expired - Lifetime EP0352597B1 (fr) 1988-07-28 1989-07-18 Procédé de fabrication de feuillard laminé à chaud ou tôles fortes

Country Status (8)

Country Link
US (1) US4994118A (fr)
EP (1) EP0352597B1 (fr)
JP (1) JPH02175816A (fr)
KR (1) KR900001424A (fr)
AT (1) ATE107708T1 (fr)
CA (1) CA1318838C (fr)
DE (2) DE3825634C2 (fr)
ES (1) ES2058410T3 (fr)

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CN114178314A (zh) * 2021-12-09 2022-03-15 福建三宝钢铁有限公司 一种低合金高强度热轧卷板q390c轧制工艺
CN115254958A (zh) * 2022-06-23 2022-11-01 山东科技大学 一种利用温轧析出β-Mn相强化TWIP钢的方法

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JPH0688125A (ja) * 1992-09-09 1994-03-29 Aichi Steel Works Ltd 連続鋳造片及び鋼塊の熱間加工法
DE4498699B4 (de) * 1993-11-09 2005-04-07 Nisshin Steel Co., Ltd. Verwendung eines Rostfreien Stahls mit ausgezeichnetem Korrosionswiderstand gegenüber Salzschmelzen
KR0169172B1 (ko) * 1994-02-15 1999-01-15 아키모토 유우미 철-크롬계 합금
KR100334253B1 (ko) * 1999-11-22 2002-05-02 장인순 고온 용융염에서 내부식성이 우수한 합금강
JP4774633B2 (ja) * 2001-06-04 2011-09-14 大同特殊鋼株式会社 マルテンサイト系耐熱鋼の製造方法
DE10215598A1 (de) * 2002-04-10 2003-10-30 Thyssenkrupp Nirosta Gmbh Nichtrostender Stahl, Verfahren zum Herstellen von spannungsrißfreien Formteilen und Formteil
DE10215597A1 (de) * 2002-04-10 2003-10-30 Thyssenkrupp Nirosta Gmbh Verfahren zum Herstellen eines hohe Kohlenstoffgehalte aufweisenden martensitischen Stahlbands und Verwendung eines solchen Stahlbands
JP4883546B2 (ja) * 2002-09-20 2012-02-22 Ｊｘ日鉱日石金属株式会社 タンタルスパッタリングターゲットの製造方法
JP4263900B2 (ja) * 2002-11-13 2009-05-13 日鉱金属株式会社 Ｔａスパッタリングターゲット及びその製造方法
CN1771350A (zh) * 2003-04-01 2006-05-10 株式会社日矿材料 钽溅射靶及其制造方法
EP1681368B1 (fr) * 2003-11-06 2021-06-30 JX Nippon Mining & Metals Corporation Methode de production d'une cible de pulverisation de tantale
CN101171362B (zh) * 2005-04-28 2010-06-09 日矿金属株式会社 溅射靶
US20060275168A1 (en) * 2005-06-03 2006-12-07 Ati Properties, Inc. Austenitic stainless steel
SE529003E (sv) 2005-07-01 2011-10-11 Sandvik Intellectual Property Ni-Cr-Fe-legering för högtemperaturanvändning
CN101278071B (zh) * 2005-10-04 2010-08-11 日矿金属株式会社 溅射靶
JP4943219B2 (ja) * 2007-04-26 2012-05-30 山陽特殊製鋼株式会社 高強度で熱間加工性が良好なＭｏ、Ｔｉ含有オーステナイト系ステンレス鋼
CN101348888A (zh) 2007-07-18 2009-01-21 青岛三庆金属有限公司 低镍奥氏体不锈钢及其制备方法
DE102007060133A1 (de) * 2007-12-13 2009-06-18 Witzenmann Gmbh Leitungsteil aus nickelarmem Stahl für eine Abgasanlage
ES2925948T3 (es) 2015-12-14 2022-10-20 Swagelok Co Piezas forjadas de acero inoxidable altamente aleado elaboradas sin recocido en solución
DE102016109253A1 (de) * 2016-05-19 2017-12-07 Böhler Edelstahl GmbH & Co KG Verfahren zum Herstellen eines Stahlwerkstoffs und Stahlwerksstoff
CN111041179B (zh) * 2019-12-03 2021-12-14 马鞍山钢铁股份有限公司 一种消除高Cr当量P92耐热钢高温铁素体的方法及高Cr当量P92耐热钢的制备方法
RU2735777C1 (ru) * 2020-05-07 2020-11-09 Федеральное государственное автономное образовательное учреждение высшего образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") Способ получения катаных полуфабрикатов из аустенитной коррозионностойкой стали
EP3974072B1 (fr) 2020-09-24 2023-07-19 Primetals Technologies Austria GmbH Installation combinée de coulée et de laminage et procédé de fonctionnement de l'installation combinée de coulée et de laminage
CN112496037B (zh) * 2020-11-16 2021-11-23 太原钢铁(集团)有限公司 一种镍基合金板材轧制方法
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FR2549491A1 (fr) * 1983-07-22 1985-01-25 Nippon Kokan Kk Procede de fabrication de plaques d'acier austenitique inoxydable
EP0144694A2 (fr) * 1983-11-02 1985-06-19 BROWN, BOVERI & CIE Aktiengesellschaft Procédé de fabrication de demi-produits en acier inoxydable austénitique ou martensitique
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Publication number Priority date Publication date Assignee Title
US4360391A (en) * 1981-05-22 1982-11-23 Nisshin Steel Co., Ltd. Process for production of coil of hot rolled strip of austenitic stainless steel
FR2549491A1 (fr) * 1983-07-22 1985-01-25 Nippon Kokan Kk Procede de fabrication de plaques d'acier austenitique inoxydable
EP0144694A2 (fr) * 1983-11-02 1985-06-19 BROWN, BOVERI & CIE Aktiengesellschaft Procédé de fabrication de demi-produits en acier inoxydable austénitique ou martensitique
DE3617907A1 (de) * 1985-05-29 1986-12-04 Nippon Kokan K.K., Tokio/Tokyo Verfahren zur herstellung von austenitischen rostfreien stahlplatten mit hoher korrosionsfestigkeit und hoher mechanischer festigkeit bei umgebungstemperatur und bei hohen temperaturen

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114178314A (zh) * 2021-12-09 2022-03-15 福建三宝钢铁有限公司 一种低合金高强度热轧卷板q390c轧制工艺
CN115254958A (zh) * 2022-06-23 2022-11-01 山东科技大学 一种利用温轧析出β-Mn相强化TWIP钢的方法

Also Published As

Publication number Publication date
DE3825634A1 (de) 1990-02-01
KR900001424A (ko) 1990-02-27
EP0352597B1 (fr) 1994-06-22
DE3825634C2 (de) 1994-06-30
US4994118A (en) 1991-02-19
DE58907934D1 (de) 1994-07-28
ES2058410T3 (es) 1994-11-01
ATE107708T1 (de) 1994-07-15
CA1318838C (fr) 1993-06-08
JPH02175816A (ja) 1990-07-09

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