US3928083A - Process for producing an enamelling steel sheet - Google Patents

Process for producing an enamelling steel sheet Download PDF

Info

Publication number
US3928083A
US3928083A US448958A US44895874A US3928083A US 3928083 A US3928083 A US 3928083A US 448958 A US448958 A US 448958A US 44895874 A US44895874 A US 44895874A US 3928083 A US3928083 A US 3928083A
Authority
US
United States
Prior art keywords
steel
titanium
content
steel sheet
amount
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.)
Expired - Lifetime
Application number
US448958A
Other languages
English (en)
Inventor
Hisashi Gondo
Hiroshi Takechi
Kazuo Namba
Matsuo Usuda
Kouichi Kawasaki
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.)
Nippon Steel Corp
Original Assignee
Nippon Steel Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Application granted granted Critical
Publication of US3928083A publication Critical patent/US3928083A/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold 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
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing

Definitions

  • PROCESS FOR PRODUCING AN ENAMELLING STEEL SHEET Inventors: Hisashi Gondo; Hiroshi Takechi;
  • ABSTRACT A process for producing an enamelling steel sheet which comprises tapping molten steel with manganese content not more than 0.40%, lowering the carbon content in the molten steel to not more than 0.01%, adding titanium to the molten steel in an amount enough to obtain a titanium content between 0.01 and 0.3%, preferably between 0.03 and 0.1%, and also adding one or more of rare earth elements such as lanthanum, cerium, neodymium, praseodymium, and samarium (hereinafter called Rem) in total amount between 0.01 and 0.15%, preferably 0.02 and 0.12%, casting the molten steel into ingot or slab, hot rolling and then cold rolling the ingot or slab preferably at a cold rolling rate between 30 and 90% and then annea
  • Rare earth elements such as lanthanum, cerium, neodymium, praseodymium, and samarium
  • an enamelling steel sheet It is required for an enamelling steel sheet that it is free from the surface defect due to hydrogen, namely, fish-scale, and it has good adhesion to enamelling glaze. At the same time, the enamelling steel sheet is required to have good workability such as deep-drawing because the enamelling steel sheet is very often subjected to severe forming into bath tubs, tableware, sanitary utensiles and so on and then enamelled. It is also required in case of single application of enamelling glaze that the enamelling steel sheet is free from surface defects due to carbonaceous gas, such as foams and blisters as well Free from the strain due to enamel firing and that it has a large acid-pickling rate from the point of productivity.
  • carbonaceous gas such as foams and blisters
  • titanium is added to the steel to fix carbon and nitrogen in the steel so as to render the steel non-aging and to improve resistance against the fish-scale by the titanium content in the steel.
  • the amount of titanium to be added to fix the carbonincreases, the steel hardens and the production cost increases.
  • the steel sheet produced by the above conventional methods hasa. defect that surface defects due to titanium compounds appear on the steel surface in some cases, thus causing lowering ofthe production yield. Also in case wheretitanium is added to the steel, the weight decreases during the acid pickling treatment conducted as a preliminary treatment for the enamel firing is relatively small so that the time required for the preliminary treatment is necessitated to be longer in case of the single application 'of enamelling glaze. This is undesirable from the point of the productivity.
  • one of the objects of the present invention is to provide a process for producing an enamelling steel sheet having remarkably excellent resistance against the fish-scale and free from the above defects.
  • a process for producing an emamelling steel sheet which comprises tapping molten steel with manganese content not more than 0.40%, lowering the carbon content in the molten steel to not more than 0.01%, adding titanium to the moltenv steel in an amount enough to obtain a titanium content between 0.01 and 0.3%, preferably between 0.03 and 0.1%, and also adding one or more of rare earth elements such as lanthanum, cerium, neodymium, praseodymium, and samarium (hereinafter called Rem) in total amount between 0.01 and 0.15%, preferably 0.02 and 0.12%, casting the molten steel into ingot or slab, hot rolling and then cold rolling the ingot or slab preferably at a cold rolling rate between 30 and 90% and then annealing the steel sheet.
  • rare earth elements such as lanthanum, cerium, neodymium, praseodymium, and samarium
  • a process for producing an enamelling steel sheet which comprises tapping molten steel with a manganese content not more than 0.40%, lowering the carbon content in the steel to not more than 0.01% by vacuum degassing, leaving the steel after casting to ingot mold until an initial solidified layer is formed, adding titanium and Rem to the non-solidified portion in an amount to obtain a titanium content between 0.01 and 0.3%, preferably 0.03 and 0.1%, and a total content of Rem between 0.01 and 0.15%, preferably between 0.02 and 0.12%, casting the steel into ingot, hot rolling and cold rolling the steel preferably with a cold rolling reduction rate between 30 and and then annealing the steel sheet.
  • FIG. 1 shows the initial solidified layer thickness of the steel sheet (A) produced according to the present invention.
  • the molten steel is tapped with a manganese content not more than 0.40%.
  • a smaller manganese content is desirable for reducing the strain due to the enamel firing as well as from the point of material quality, and thus its upper limit is defined as 0.40%.
  • the molten steel is subjected to vacuum degassing treatment to lower the carbon content to not more than 0.01%.
  • the reason for limiting the carbon content to not more than 0.01% is to prevent occurrence of the surface defects such as foams and blisters due to the carbonaceous gas and to prevent the strain due to the enamel firing.
  • the oxygen content is also reduced by the degassing, but the remaining oxygen can be further reduced by a preliminary deoxydation with aluminum, for example, after the completion of the degassing treatment, if necessary.
  • titanium and Rem Prior to the pouring the molten steel into the ingot mold or during the pouring, titanium and Rem are added to the molten steel so as to obtain a titanium content between 0.01 and 0.30%, preferably 0.03 and 0.10% and a total Rem content between 0.01 and 0.15%, preferably 0.03 and 0.12%.
  • the reason for limiting the titanium content in the steel between 0.01 and 0.30%, preferably 0.03 and 0.10% is that if the titanium content is more than 0.30%, the steel hardens and press formability is lowered and the production cost increases, while the titanium content is less than 0.01%, no substantial improvement on the resistance against the fish-scale and deep-drawability can be expected.
  • the reason for limiting the Rem content between 0.01 and 0.15%, preferably 0.02 and 0.12% is that a Rem content more than 0.15% will cause increased production cost and, on the other hand, a Rem content less than 0.01% no substantial improvement on the resistance against the fish-scale 3 can be expected.
  • the steel slab produced according to the present invention is subjected to hot rolling, acid pickling, electrical cleaning, annealing and, if necessary, temper rolling.
  • the hot rolling may be conducted under ordinary conditions, but desirable results can be obtained by conducting the hot rolling with coiling temperature between 450 and 800C, preferably 550 and 730C. If the hot coiling temperature exceeds 800C, it is difficult to adjust the temperature, and on the other hand if the coiling temperature is lower than 450C the improvement effect of the resistance against the fish-scale is reduced.
  • a reduction rate not less than is desirable for obtaining desirable material quality, but with a reduction rate more than 90% the required thickness of the hot rolled steel sheet is too thick for practical use. On the other hand, with a reduction rate less than 30%, desired deep-drawability can not be obtained.
  • the annealing may be done by any of a box annealing, a continuous annealing and other annealing methods, and the annealing temperature should be between 650 and 1000C, preferably between 650 and 910C in case of the box annealing and an open coil annealing, and between 700 and 980C in case of the continuous annealing. If the annealing temperature is lower than the lower limit, softening of the steel caused by recrystallization is not enough so that desirable workability is not obtained. On the other hand, if the temperature is higher than the upper limit, the amount of transformation into austenite is large so that good deep-drawability can not be obtained, and the higher temperature is not desirable also from the point of the economy of the furnace.
  • the present inventors have conducted further extensive studies and experiments for solving the problems such as the occurrence of the surface defects due to the titanium compounds and the lowering of the weight decrease during the acid pickling, and have found that these problems can be solved by forming an initial solidified layer containing no titanium on the steel surface according to the present invention as defined in the paragraphs (2) and (3) as hereinbefore stated.
  • the present invention of the paragraph (2) may be conducted as under.
  • Molten steel containing not more than 0.40% of manganese preferably not more than 0.25% of manganese is tapped, and subjected to vacuum degassing to reduce the carbon content to less than 0.01%, and then prior to or at the same time of pouring the molten steel into an ingot mold, Rem is added so as to obtain a total Rem content between 0.01 and 0.15%, preferably 0.02 and 0.12%, and the steel is left after the pouring into the mold until an initial solidified layer is formed, and titanium is added to the non-solidified portion so as to obtain a titanium content between 0.01 and 0.3%, preferably 0.03 and 0.10%.
  • Rem may be added together with titanium to the non-solidified portion of the ingot after the molten steel is cast into the mold and the initial solidified layer containing no titanium and Rem is formed according to the present invention defined in the paragraph 3).
  • molten steel with a manganese content not more than 0.40%, preferably not more than 0.25% is tapped and subjected to vacuum degassing treatment to lower the carbon content to not more than 0.01%, and the molten steel is left after it is cast into the mold until an initial solidified layer is formed, and then titanium and Rem are added to the non-solidified portion so as to obtain a titanium content between 0.01 and 0.3%, preferably 0.03 and 0.1%, and a total Rem content between 0.01 and 0.15%, preferably 0.02 and 0.12%.
  • the initial solidified layer produced by the present invention as defined in the paragraphs (2) and (3) is different from the conventional rim layer formed by the rimming action in their formation mechanisms, and it is the important difference that the initial solidified layer is formed without rimming action, and thus the surface of the ingot produced by the present invention is as good as that of the rimmed steel. Further as the initial solidified layer of the steel produced by the present invention does not contain titanium, surface defects due to the titanium compounds are not caused at all, and the cold rolled steel sheets produced according to the present invention do not contain titanium in their surface layer and thus their weight decrease in acid pickling is large enough so that the time required by the acid pickling treatment is largely reduced.
  • Rem is added in the ladle as in the paragraph (2) of the present invention, good uniformity of the Rem addition in the steel is assured, and in case of the paragraph (3) of the present invention, a remarkably good yield of Rem is assured.
  • Molten steel prepared in a converter, having a ladle analysis showing 0.018% of carbon and 0.17% of manganese was subjected to vacuum degassing and predeoxidized by addition of aluminum.
  • the molten steel was left one minute after casting into an ingot mold to form an initial solidified layer in the ingot, and titanium and Rem were added to the non-solidified portion.
  • the steel B Rem was added simultaneously when the ingot-casting of the molten steel was started, and the molten steel was left 1 minute after the casting to form an initial solidified layer, and titanium was added to the non-solidified portion.
  • titanium and Rem were added simultaneously when the ingot-casting was started.
  • the molten steel was left one minute after the ingot-casting to form an initial solidified layer in the steel ingot, and titanium was added to the non-solidified layer (steel D) and Rem was added to the non-solidified layer (steel E).
  • All of the inventive steels A, B, and C and the comparative steels D and E were hot rolled to 6.5mm thickness with a hot coiling temperature of 590C, cold rolled to 2.0mm thickness, and subjected to a box annealing at 700C for 12 hours and 1% temper rolling.
  • inventive steels A, B, and C were immersed T bl 5 in 10% H 80 solution at 70C for 10 minutes and a 6 measured for weight decrease by acid pickling.
  • the Inventive S e Hyd g Permeation Time results are shown in Table 3.
  • the inventive steels A and A 168 B showed a remarkably large weight decrease and were g 13 7 found to be very advantageous for efficiency of enamel Comparative Stee] firing.
  • a process for producing an enamelling steel sheet which comprises tapping molten steel with a manganese content of not more than 0.40%, lowering the carbon content in the molten steel to not more than 0.01%, adding titanium to the molten steel in an amount enough to obtain a titanium content between 0.01 and 0.3%, and adding one or more elements selected from the group consisting of the rare earth elements in a total amount between 0.01 and 0.15%, casting the molten steel into ingot or slab, hot rolling and then cold rolling the ingot or slab and then annealing the steel sheet.
  • the rare earth element is lanthanum, cerium, neodymium, praseodymium or samarium.
  • a process for producing an enamelling steel sheet which comprises tapping molten steel with a manganese content ot not more than 0.40%, lowering the carbon content in the molten steel to not more than 0.01% by vacuum degassing, adding one or more elements selected from the group consisting of the rare earth elements to the steel in a total amount between 0.01 and 0.15%, prior to or at the same time of casting the steel into an ingot mold, leaving the steel after casting in the mold until an initial solidified layer is formed, adding titanium to the non-solidified portion so as to obtain a titanium content between 0.01 and 0.3%, and hot rolling, cold rolling and annealing the steel sheet.
  • a process for producing an enamelling steel sheet which comprises tapping molten steel with a manganese content of not more than 0.40%, lowering the carbon content in the steel to not more than 0.01% by vacuum degassing, leaving the steel after casting in an ingot mold until an initial solidified layer is formed, adding titanium and an element selected from the group consisting of one or more of the rare earth elements to the non-solidified portion in an amount to obtain a titanium content between 0.01 and 0.3%, and a total content of the rare earth elements between 0.01 and 0.15%, casting the steel into an ingot, hot rolling and cold rolling the steel, and then annealing the steel sheet.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
US448958A 1973-03-09 1974-03-07 Process for producing an enamelling steel sheet Expired - Lifetime US3928083A (en)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2716973A JPS543447B2 (no) 1973-03-09 1973-03-09

Publications (1)

Publication Number Publication Date
US3928083A true US3928083A (en) 1975-12-23

Family

ID=12213543

Family Applications (1)

Application Number Title Priority Date Filing Date
US448958A Expired - Lifetime US3928083A (en) 1973-03-09 1974-03-07 Process for producing an enamelling steel sheet

Country Status (3)

Country Link
US (1) US3928083A (no)
JP (1) JPS543447B2 (no)
DE (1) DE2410826B2 (no)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4092179A (en) * 1976-12-27 1978-05-30 Jones & Laughlin Steel Corporation Method of producing high strength cold rolled steel sheet
US4290805A (en) * 1978-04-06 1981-09-22 Compagnie Universelle D'acetylene Et D'electro-Metallurgie Method for obtaining iron-based alloys allowing in particular their mechanical properties to be improved by the use of lanthanum, and iron-based alloys obtained by the said method
US4313770A (en) * 1979-06-28 1982-02-02 Sumitomo Metal Industries, Ltd. Method of producing cold rolled steel strip having improved press formability and bake-hardenability
US4328032A (en) * 1980-03-13 1982-05-04 Sybron Corporation Titanium and niobium high strength steel alloys
AU677535B2 (en) * 1994-12-20 1997-04-24 Pohang Iron & Steel Co., Ltd. Method for manufacturing a cold rolled steel sheet with excellent enamel adherence
US20050121439A1 (en) * 2002-03-14 2005-06-09 Ssw Holding Company, Inc. Porcelain oven rack
US20070272231A1 (en) * 2006-05-25 2007-11-29 Ssw Holding Company, Inc. Oven rack having an integral lubricious, dry porcelain surface
US11236427B2 (en) 2017-12-06 2022-02-01 Polyvision Corporation Systems and methods for in-line thermal flattening and enameling of steel sheets

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5722974B2 (no) * 1975-01-28 1982-05-15
JPS5743626A (en) * 1980-08-26 1982-03-11 Nisshin Flour Milling Co Water cooling method of animal feeding enviroment
JPS5838255U (ja) * 1981-09-08 1983-03-12 誠和化学株式会社 温室カ−テン開閉装置
JPS6019366U (ja) * 1983-07-19 1985-02-09 兼弥産業株式会社 園芸ハウスの昇温防止構造
JPS6033850U (ja) * 1983-08-17 1985-03-08 誠和化学株式会社 温室の冷却構造
JPS6049752U (ja) * 1983-09-12 1985-04-08 誠和化学株式会社 温室の冷房装置
JPS6049753U (ja) * 1983-09-16 1985-04-08 誠和化学株式会社 温室の冷房装置
JP4780084B2 (ja) * 1998-03-30 2011-09-28 Ｊｆｅスチール株式会社 表面性状の良好なチタンキルド鋼材およびその製造方法
KR100360095B1 (ko) * 1998-08-28 2003-10-22 주식회사 포스코 성형성이 우수한 고밀착 법랑강판의 제조방법
CN115478209B (zh) * 2021-05-31 2023-08-11 宝山钢铁股份有限公司 一种拉深性能良好的热轧酸洗搪瓷钢及其生产方法

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3666570A (en) * 1969-07-16 1972-05-30 Jones & Laughlin Steel Corp High-strength low-alloy steels having improved formability
US3666452A (en) * 1969-07-16 1972-05-30 Jones & Laughlin Steel Corp High-strength low-alloy steels
US3671336A (en) * 1969-07-16 1972-06-20 Jones & Laughlin Steel Corp High-strength plain carbon steels having improved formability

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS4987514A (no) * 1972-12-26 1974-08-21

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3666570A (en) * 1969-07-16 1972-05-30 Jones & Laughlin Steel Corp High-strength low-alloy steels having improved formability
US3666452A (en) * 1969-07-16 1972-05-30 Jones & Laughlin Steel Corp High-strength low-alloy steels
US3671336A (en) * 1969-07-16 1972-06-20 Jones & Laughlin Steel Corp High-strength plain carbon steels having improved formability

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4092179A (en) * 1976-12-27 1978-05-30 Jones & Laughlin Steel Corporation Method of producing high strength cold rolled steel sheet
US4290805A (en) * 1978-04-06 1981-09-22 Compagnie Universelle D'acetylene Et D'electro-Metallurgie Method for obtaining iron-based alloys allowing in particular their mechanical properties to be improved by the use of lanthanum, and iron-based alloys obtained by the said method
US4313770A (en) * 1979-06-28 1982-02-02 Sumitomo Metal Industries, Ltd. Method of producing cold rolled steel strip having improved press formability and bake-hardenability
US4328032A (en) * 1980-03-13 1982-05-04 Sybron Corporation Titanium and niobium high strength steel alloys
AU677535B2 (en) * 1994-12-20 1997-04-24 Pohang Iron & Steel Co., Ltd. Method for manufacturing a cold rolled steel sheet with excellent enamel adherence
US5738738A (en) * 1994-12-20 1998-04-14 Pohang Iron & Steel Co., Ltd. Method for manufacturing a cold rolled steel sheet with excellent enamel adherence
US20050121439A1 (en) * 2002-03-14 2005-06-09 Ssw Holding Company, Inc. Porcelain oven rack
US7290320B2 (en) 2002-03-14 2007-11-06 Ssw Holding Company, Inc. Method of forming a steel wire oven rack for later porcelain coating
US20070272231A1 (en) * 2006-05-25 2007-11-29 Ssw Holding Company, Inc. Oven rack having an integral lubricious, dry porcelain surface
US20100059041A1 (en) * 2006-05-25 2010-03-11 Ssw Holdings Oven Rack Having Integral Lubricious, Dry Porcelain Surface
US8739773B2 (en) * 2006-05-25 2014-06-03 Ssw Holding Company, Inc. Oven rack having integral lubricious, dry porcelain surface
US11236427B2 (en) 2017-12-06 2022-02-01 Polyvision Corporation Systems and methods for in-line thermal flattening and enameling of steel sheets

Also Published As

Publication number Publication date
DE2410826A1 (de) 1974-09-19
JPS543447B2 (no) 1979-02-23
DE2410826B2 (de) 1977-04-14
JPS49115018A (no) 1974-11-02

Similar Documents

Publication Publication Date Title
US3928083A (en) Process for producing an enamelling steel sheet
EP0041354B1 (en) Method for producing cold rolled steel sheets having a noticeably excellent formability
KR100233690B1 (ko) 극저탄소 냉간압연강판 제조 방법
JPS5942742B2 (ja) 降伏比の低い深絞り用高強度冷延鋼板
US3950191A (en) Cold rolled steel sheets having an excellent enamelability and a method for producing said cold rolled steel sheets
KR100361846B1 (ko) 가공성이 우수한 박판용 강 및 그 탈산방법
US3335036A (en) Deep drawing steel sheet and method for producing the same
JPH06102810B2 (ja) 二次加工性に優れた深絞り用合金化溶融亜鉛メッキ鋼板の製造方法
KR950003535B1 (ko) 내피쉬스케일성이 우수한 법랑용 강판 및 그 제조방법
JPS582248B2 (ja) 加工性のすぐれた溶融メツキ鋼板の製造法
KR20200066199A (ko) 법랑용 강판 및 그 제조방법
CA1178182A (en) Process for preparing aluminum-plated steel sheets having low yield strength and high oxidation resistance
JPS6048571B2 (ja) 深絞り用合金化亜鉛メツキ鋼板の製造法
KR0135001B1 (ko) 소부경화형 연질 표면처리 열연코일의 제조방법
JPS6013052A (ja) 超深絞り用冷延鋼板
JPS633930B2 (no)
JPH0735527B2 (ja) 耐加熱黒変性に優れた溶融Ａｌめっき鋼板用鋳片の製造方法
KR100361753B1 (ko) 박슬라브 직접압연법을 이용한 열연법랑강판 제조방법
KR100244659B1 (ko) 기포발생이 없는 고가공용 법랑용 냉연강판의 제조방법
JP2857761B2 (ja) 耐爪とび性の優れた連続鋳造製ほうろう用鋼板の製造法
JPS5935657A (ja) ほうろう特性および成形性に優れるほうろう用冷延鋼板
JPH02236254A (ja) 耐爪とび性と溶接性の優れた連続鋳造製ほうろう用鋼板およびその製造方法
JPS582263B2 (ja) 加工性および表面性状のすぐれた薄鋼板
JPS59229463A (ja) 連続鋳造による加工性の優れたほうろう用冷延鋼板の製造方法
KR20050068250A (ko) 법랑용 강판 및 그 제조 방법