US20140205802A1 - Cast product having alumina barrier layer - Google Patents

Cast product having alumina barrier layer Download PDF

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Publication number
US20140205802A1
US20140205802A1 US14/220,280 US201414220280A US2014205802A1 US 20140205802 A1 US20140205802 A1 US 20140205802A1 US 201414220280 A US201414220280 A US 201414220280A US 2014205802 A1 US2014205802 A1 US 2014205802A1
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United States
Prior art keywords
mass
barrier layer
specimen
cast
alumina barrier
Prior art date
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Abandoned
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US14/220,280
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English (en)
Inventor
Youhei Enjo
Makoto Hineno
Shinichi Uramaru
Kunihide Hashimoto
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.)
Kubota Corp
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Kubota Corp
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Filing date
Publication date
Priority claimed from JP2012067828A external-priority patent/JP6005963B2/ja
Priority claimed from JP2012067827A external-priority patent/JP5977054B2/ja
Priority claimed from JP2013010883A external-priority patent/JP6068158B2/ja
Application filed by Kubota Corp filed Critical Kubota Corp
Assigned to KUBOTA CORPORATION reassignment KUBOTA CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: ENJO, YOUHEI, HASHIMOTO, KUNIHIDE, HINENO, MAKOTO, URAMARU, SHINICHI
Publication of US20140205802A1 publication Critical patent/US20140205802A1/en
Priority to US16/227,970 priority Critical patent/US11072847B2/en
Abandoned legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/02—Pretreatment of the material to be coated
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/10—Oxidising
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D13/00—Centrifugal casting; Casting by using centrifugal force
    • B22D13/02—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D29/00—Removing castings from moulds, not restricted to casting processes covered by a single main group; Removing cores; Handling ingots
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/052—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 40%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/053—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 30% but less than 40%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/10—Oxidising
    • C23C8/12—Oxidising using elemental oxygen or ozone
    • C23C8/14—Oxidising of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/10—Oxidising
    • C23C8/16—Oxidising using oxygen-containing compounds, e.g. water, carbon dioxide
    • C23C8/18—Oxidising of ferrous surfaces
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/34—Coated articles, e.g. plated or painted; Surface treated articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/06—Cast-iron alloys
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
    • Y10T428/24355—Continuous and nonuniform or irregular surface on layer or component [e.g., roofing, etc.]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
    • Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
    • Y10T428/264—Up to 3 mils
    • Y10T428/265—1 mil or less

Definitions

  • the present invention relates to a cast product having an alumina barrier layer, and a method for producing the same.
  • austenite-based heat resistant alloys that are excellent in high temperature strength are used because they are exposed to a high temperature atmosphere.
  • a metal oxide layer is formed on the surface during use in a high temperature atmosphere, and this oxide layer serves as a barrier to protect the base material in the high temperature atmosphere.
  • Al is a ferrite generating element, it will deteriorate the ductility of the material, and decrease high temperature strength when the content is too large. This ductility decreasing tendency is observed, in particular, when the content of Al exceeds 4%.
  • the austenite-based heat resistant alloys in the above patent documents have a disadvantage of causing deterioration in ductility of a base material although they are expected to improve the barrier function by Al 2 O 3 .
  • WO 2010/113830 proposes a cast product in which an alumina barrier layer containing Al 2 O 3 is formed on the inner surface of the cast body, and Cr base particles having higher Cr concentration than the base material matrix are dispersed at the boundary between the alumina barrier layer and the cast body, by conducting an inner surface process so that the surface roughness (Ra) of the cast body is 0.05 ⁇ m to 2.5 ⁇ m, followed by a heat treatment in an oxidizing atmosphere, for providing a cast product capable of ensuring high temperature stability of an alumina barrier layer without making the Al content exceeding 4%, and capable of exerting excellent barrier function in a high temperature atmosphere without deteriorating the ductility of the material.
  • Ra surface roughness
  • the cast product in WO 2010/113830 is able to keep the excellent oxidation resistance, cementation resistance, nitriding resistance, corrosion resistance and so on for a long term in use in a high temperature atmosphere owing to the presence of the stable alumina barrier layer.
  • the polishing such as the honing process cannot be effected over the entire length as described above, and a part having large surface roughness can be left. As a result, in these parts, desired Al 2 O 3 film cannot be formed in some cases.
  • a so-called U-shaped tube having a bent portion is produced by bending a straight tube having previously subjected to a surface treatment and a heat treatment by processing.
  • the alumina barrier layer formed on the surface of the straight tube can peel off due to strain or the like occurring in the bent portion at the time of bending the straight tube. This phenomenon is significantly observed, in particular, on the ventral side, or the inner side of the bent portion.
  • an alumina barrier layer by conducting a heat treatment after joining the cast products having subjected to a surface treatment by welding, however, in this case, metal oxides mainly composed of Cr oxides are formed, in particular, in the welded part, and an alumina barrier layer having sufficient cementation resistance cannot be formed.
  • a welded part not formed with an alumina barrier layer allows entry of oxygen, carbon, nitrogen and the like from the external atmosphere and cannot prevent oxidation, carbonization and nitriding for a long term.
  • a cast product having an alumina barrier layer is a cast product including an alumina barrier layer containing Al 2 O 3 formed on the surface of a cast body, and the cast body contains C: 0.3 mass % to 0.7 mass %, Si: 0.1 mass % to 1.5 mass %, Mn: 0.1 mass % to 3 mass %, Cr: 15 mass % to 40 mass %, Ni: 20 mass % to 55 mass %, Al: 2 mass % to 4 mass %, rare earth element: 0.005 mass % to 0.4 mass %, W: 0.5 mass % to 5 mass % and/or Mo: 0.1 mass % to 3 mass %, and 25 mass % or more of Fe, and an inevitable impurity, and 80 mass % or more of the rare earth element is La.
  • a method for producing a cast product having an alumina barrier layer on the surface according to the present invention is a method for producing a cast product for use in a high temperature atmosphere, and the method including:
  • a method for producing a cast product according to the present invention is a method for producing a cast product for use in a high temperature atmosphere, obtainable by joining a first cast body and a second cast body made of a heat resistant alloy containing 15 mass % or more of Cr, 20 mass % or more of Ni, and 2 mass % to 4 mass % of Al by welding, and the method includes: the step of joining the first cast body and the second cast body by welding;
  • the cast product having an alumina barrier layer of the present invention is a cast product for use in a high temperature atmosphere, formed by joining a first cast body and a second cast body made of a heat resistant alloy containing 15 mass % or more of Cr, 20 mass % or more of Ni, and 2 mass % to 4 mass % of Al by welding, and the welded part between the first cast body and the second cast body is covered with an alumina barrier layer containing Al 2 O 3 .
  • FIG. 1 is a surface photograph of specimen No. 201 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 2 is a surface photograph of specimen No. 202 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 3 is a surface photograph of specimen No. 203 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 4 is a surface photograph of specimen No. 204 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 5 is a surface photograph of specimen No. 205 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 6 is a surface photograph of specimen No. 206 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 7 is a surface photograph of specimen No. 207 which is an inventive example in Example 2 after acid treatment and before heat treatment;
  • FIG. 8 is a surface photograph of specimen No. 311 which is a reference example in Example 2 after acid treatment and before heat treatment;
  • FIG. 9 is a surface photograph of specimen No. 312 which is a reference example in Example 2 after acid treatment and before heat treatment;
  • FIG. 10 is a surface photograph of specimen No. 421 which is a comparative example in Example 2 before heat treatment (without acid treatment);
  • FIG. 11 is a surface photograph of specimen No. 201 which is an inventive example in Example 2 after heat treatment;
  • FIG. 12 is a surface photograph of specimen No. 202 which is an inventive example in Example 2 after heat treatment;
  • FIG. 13 is a surface photograph of specimen No. 203 which is an inventive example in Example 2 after heat treatment;
  • FIG. 14 is a surface photograph of specimen No. 204 which is an inventive example in Example 2 after heat treatment;
  • FIG. 15 is a surface photograph of specimen No. 205 which is an inventive example in Example 2 after heat treatment;
  • FIG. 16 is a surface photograph of specimen No. 206 which is an inventive example in Example 2 after heat treatment;
  • FIG. 17 is a surface photograph of specimen No. 207 which is an inventive example in Example 2 after heat treatment;
  • FIG. 18 is a surface photograph of specimen No. 311 which is a reference example in Example 2 after heat treatment;
  • FIG. 19 is a surface photograph of specimen No. 312 which is a reference example in Example 2 after heat treatment;
  • FIG. 20 is a surface photograph of specimen No. 421 which is a comparative example in Example 2 after heat treatment;
  • FIG. 21 is a section SEM photograph of specimen No. 201 which is an inventive example in Example 2;
  • FIG. 22 is a section SEM photograph of specimen No. 202 which is an inventive example in Example 2;
  • FIG. 23 is a section SEM photograph of specimen No. 203 which is an inventive example in Example 2;
  • FIG. 24 is a section SEM photograph of specimen No. 204 which is an inventive example in Example 2;
  • FIG. 25 is a section SEM photograph of specimen No. 205 which is an inventive example in Example 2;
  • FIG. 26 is a section SEM photograph of specimen No. 206 which is an inventive example in Example 2;
  • FIG. 27 is a section SEM photograph of specimen No. 207 which is an inventive example in Example 2;
  • FIG. 28 is a section SEM photograph of specimen No. 311 which is a reference example in Example 2;
  • FIG. 29 is a section SEM photograph of specimen No. 312 which is a reference example in Example 2;
  • FIG. 30 is a section SEM photograph of specimen No. 421 which is a comparative example in Example 2;
  • FIG. 31 is a section photograph taken by axially cutting specimen tube No. 504 which is an inventive example in Example 3;
  • FIG. 32 is a section photograph taken by axially cutting specimen tube No. 613 which is a comparative example in Example 3;
  • FIG. 33 is a section photograph of a specimen piece obtained from specimen tube No. 504 which is an inventive example in Example 3, taken perpendicularly to a welded part;
  • FIG. 34 is a section photograph of a specimen piece obtained from specimen tube No. 613 which is a comparative example in Example 3, taken perpendicularly to a welded part;
  • FIG. 35 is a photograph of specimen tube No. 504 which is an inventive example in Example 3 by section SEM analysis.
  • FIG. 36 is a photograph of specimen tube No. 613 which is a comparative example in Example 3 by section SEM analysis.
  • the first embodiment according to the present invention provides a cast product in which an alumina barrier layer containing Al 2 O 3 is formed on a surface of a cast body, and the cast body contains C: 0.3 mass % to 0.7 mass %, Si: 0.1 mass % to 1.5 mass %, Mn: 0.1 mass % to 3 mass %, Cr: 15 mass % to 40 mass %, Ni: 20 mass % to 55 mass %, Al: 2 mass % to 4 mass %, rare earth element: 0.005 mass % to 0.4 mass %, W: 0.5 mass % to 5 mass % and/or Mo: 0.1 mass % to 3 mass %, and 25 mass % or more of Fe in the remainder and an inevitable impurity, and 80 mass % or more of the rare earth element is occupied by La.
  • “%” is “mass %” unless otherwise specified.
  • C has a function of improving the castability and increasing the high temperature creep rupture strength. Therefore, C is contained in at least 0.3%.
  • primary carbide of Cr 7 C 3 tends to be widely formed, and migration of Al that forms the alumina barrier layer is suppressed, so that the supply of Al to the surface part of the cast body is insufficient, and the alumina barrier layer is locally fragmented and the continuity of the alumina barrier layer is impaired.
  • secondary carbide excessively precipitates, ductility and toughness are deteriorated. For this reason, the upper limit is set at 0.7%.
  • the content of C is more preferably 0.4% to 0.5%.
  • Si is contained in at least 0.1% as a deoxidant for molten alloy, for increasing the fluidity of molten alloy, and the upper limit is 1.5% because too large content will lead deterioration in high temperature creep rupture strength.
  • the upper limit of Si is more preferably 1.0%.
  • Mn is contained in at least 0.1% as a deoxidant for molten alloy, for immobilizing S in molten metal, and the upper limit is 3% because too large content will lead deterioration in high temperature creep rupture strength.
  • the upper limit of Mn is preferably 1.6%.
  • Cr is contained in 15% or more for the purpose of contribution to improvement in high temperature strength and repeated oxidation resistance.
  • the upper limit is 40% because too large content will lead deterioration in high temperature creep rupture strength.
  • Cr occupies more preferably 20% to 30%.
  • Ni is an element required for ensuring repeated oxidation resistance and stability of metal tissue.
  • the content of Ni is small, the content of Fe is relatively large, so that Cr—Fe—Mn oxide is more likely to be generated on the surface of the cast body, and hence generation of an alumina barrier layer is inhibited. For this reason, Ni is contained in 20% or more. However, since the effect of increasing the amount is no longer obtained with the content of Ni exceeding 55%, the upper limit is 55%. Ni is contained more preferably in 28% to 45%.
  • Al is an element that is effective for improving the cementation resistance and the caulking resistance. In the present invention, it is an essential element for generating an alumina barrier layer on the surface of a cast body. Therefore, Al is contained in at least 2% or more. However, when the content exceeds 4%, the ductility will be deteriorated as described above, and hence the upper limit is specified at 4% in the first embodiment of the present invention.
  • the content of Al is more preferably 2.5% to 3.8%.
  • Rare Earth Element 0.005% to 0.4%, Wherein 80% or More of the Same is La.
  • Rare earth elements mean seventeen elements including fifteen elements in the lanthanum series from La to Lu in the periodic table, as well as Y and Sc, and 80% or more of the rare earth element contained in the heat resistant alloy in the first embodiment of the present invention is La.
  • La By containing La in 80% or more, it is possible to increase the generation amount of Ni—La compounds such as Ni 2 La and Ni 3 La having excellent high temperature tensile ductility, and in particular, high temperature tensile ductility at 1100° C. or higher.
  • Rare earth elements have the ability of immobilizing S and the ability of immobilizing oxide film by rare earth oxide, and are contained in 0.005% or more for contributing to facilitation for generation and stabilization of an alumina barrier layer.
  • the upper limit is 0.4% because too large amount will deteriorate the ductility and toughness.
  • the content of Ce in the rare earth element is desirably 0.1% or less.
  • the Ce content it is possible to reduce the generation amount of Ce compounds such as Ni 2 Ce and Ni 3 Ce that cause high temperature brittleness, and to increase the high temperature tensile ductility.
  • the rare earth element does not contain Ce and is composed of only La.
  • W and Mo solid-solved in the matrix and reinforce the austenite phase of the matrix, thereby improving the creep rupture strength.
  • W and Mo solid-solved in the matrix and reinforce the austenite phase of the matrix, thereby improving the creep rupture strength.
  • at least either of W and Mo is contained, and in the case of W, 0.5% or more is contained, and in the case of Mo, 0.1% or more is contained.
  • W and Mo have a function of inhibiting generation of an alumina barrier layer by suppressing migration of Al by being solid-solved in the matrix because they have large atomic radii.
  • the content of C is large, primary carbides of (Cr, W, Mo) 7 C 3 are likely to be formed widely, and migration of Al that forms an alumina barrier layer is suppressed, so that the supply of Al to the surface part of the cast body is insufficient, and the alumina barrier layer is locally fragmented and the continuity of the alumina barrier layer is more likely to be impaired.
  • W and Mo have large atomic radii, they are solid-solved in the matrix and have the effect of preventing generation of an alumina barrier layer by suppressing migration of Al or Cr.
  • W is 5% or less, and Mo is 3% or less. More preferably, W is 0.5% to 3%, and Mo is 2% or less.
  • Ti, Zr and Nb are elements that are easy to form carbide, and are less likely to be solid-solved in the matrix compared with W and Mo, something special function on formation of an alumina barrier layer is not recognized, however, it has a function of improving the creep rupture strength.
  • At least one of Ti, Zr and Nb may be contained as is necessary. The content is 0.01% or more for Ti and Zr, and 0.1% or more for Nb.
  • the upper limit is 0.6% for Ti and Zr, and 3.0% for Nb.
  • the upper limit is 0.3% for Ti and Zr, and 1.5% for Nb.
  • B may be contained as is necessary because it has a function of reinforcing grain boundaries of a cast body.
  • the amount of B, if added, should be more than 0 to 0.1% or less because too large content will deteriorate the creep rupture strength.
  • the content of B is more preferably more than 0.01% and 0.1% or less.
  • Diffusing speeds of Al in Fe, Ni and Cr are expected to increase as the sizes of the atoms decrease. Therefore, by increasing Fe which is a smaller atom, and reducing the amount of Cr, it is possible to increase diffusion of Al in the alloy, to facilitate migration of Al, and to promote generation of film of Al 2 O 3 . Further, by reducing Cr, it is possible to inhibit generation of Cr oxide.
  • Fe is contained in 25% or more. More preferably, Fe is contained in 30% or more.
  • the cast body forming the cast product of the first embodiment of the present invention is casted to have the aforementioned composition by producing molten metal of the aforementioned element composition, followed by centrifugal casting, stationary casting and so on.
  • the obtainable cast body may have a shape suited for the intended use.
  • the first embodiment of the present invention is particularly suited for a cast body produced by centrifugal casting.
  • fine metal tissues grow radially with an orientation as the cooling by a mold progresses, and alloy tissues where Al is easy to migrate can be obtained.
  • alloy tissues where Al is easy to migrate can be obtained.
  • the heat treatment as will be described later, it is possible to obtain a cast product formed with film which is an alumina barrier layer having a smaller thickness than a conventional one, but having excellent strength even under a repetitively-heated environment in the later-described heat treatment.
  • a tube in particular, a reaction tube used under a high temperature environment can be exemplified.
  • the cast body is subjected to a heating treatment in an oxidizing atmosphere after it is surface-treated in an objective site that is to be in contact with the high temperature atmosphere during use of the product, and the surface roughness of the site is adjusted.
  • a polishing treatment can be exemplified.
  • the surface treatment is preferably conducted on the entire objective site that is to be in contact with a high temperature atmosphere during use of the product.
  • the surface treatment may be conducted so that the surface roughness (Ra) of the objective site is 0.05 ⁇ m to 2.5 ⁇ m. More desirably, the surface roughness (Ra) is 0.5 ⁇ m to 2.0 ⁇ m.
  • the surface roughness (Ra) is less than 0.05 ⁇ m, Cr is oxidized dominantly to Al, whereas when it is 0.05 ⁇ m or more, generation of Cr oxide scale can be suppressed, and an alumina barrier layer can be formed more preferably by the subsequent heat treatment. It is expected that Cr oxide scale is more likely to be generated due to the residual processing strain when it is 2.5 ⁇ m or more.
  • by adjusting the surface roughness by the surface treatment it is possible to remove the residual stress and strain in the heat-influenced part concurrently.
  • a heat treatment is conducted in the following conditions.
  • the heat treatment is carried out by conducting a heating treatment in an oxidizing atmosphere.
  • the oxidizing atmosphere means an oxidizing environment in which oxidizing gas containing 20% by volume or more of oxygen or steam or CO 2 is mixed.
  • the heating treatment is conducted at a temperature of 900° C. or higher, preferably 1000° C. or higher, and more preferably 1050° C. or higher, and the heating time is 1 hour or more.
  • the alumina barrier layer containing Al 2 O 3 formed in the cast product of the present invention is highly tight and functions as a barrier for preventing external oxygen, carbon and nitrogen from entering the base material.
  • the surface treatment is conducted in the site that is to be in contact with a high temperature atmosphere during use of the product to adjust the surface roughness of the site, and then the site is subjected to the heating treatment in an oxidizing atmosphere, and thus Al 2 O 3 can be continuously formed as an alumina barrier layer on the surface of the cast product.
  • the thickness of the alumina barrier layer formed on the cast body is preferably 0.05 ⁇ m or more and 3 ⁇ m or less for effectively exerting the barrier function.
  • the thickness of the alumina barrier layer is less than 0.05 ⁇ m, the cementation resistance may be deteriorated, whereas when it exceeds 3 ⁇ m, peeling of the alumina barrier layer may be likely to advance due to the influence of difference in heat expansion coefficient between the base material and the film.
  • the thickness of the alumina barrier layer is more preferably 0.1 ⁇ m or more and 2.5 ⁇ m or less.
  • the thickness of the alumina barrier layer is desirably 0.5 ⁇ m or more and 1.5 ⁇ m or less, and most desirably about 1 ⁇ m on average.
  • the cast product of the first embodiment according to the present invention is able to increase the tensile ductility at high temperature (concretely 1100° C. or higher) as much as possible as will be described later in Example 1 by making the content of La in the rare earth element 80%.
  • reaction tube for use as a reaction tube, in particular, it is effective to contain La in 80% or more as the rare earth element that will not be embrittled in the use temperature region of Ce (about 1100° C.).
  • the first embodiment according to the present invention 80% or more of La is contained in the rare earth element by controlling the content of Ce, and for the Ce added material and the La added material, a repetitive oxidation test in an atmospheric air under furnace cooling at 1050° C. for a retention time of 10 hours was conducted, and difference in peeling resistance of Al 2 O 3 was little observed.
  • the first embodiment according to the present invention is suitable as a cast product that is excellent in high temperature tensile ductility and is capable of effectively preventing oxygen, carbon, nitrogen and the like from entering from the external atmosphere by the alumina barrier layer.
  • a cast product formed with a so-called “alumina barrier layer” containing Al 2 O 3 on the surface is obtained by conducting a surface treatment by an acid treatment on a heat resistant alloy containing 15% or more of Cr and 20% or more of Ni, and 2% to 4% of Al, and then conducting a heat treatment.
  • Cr is contained in 15% or more, and the upper limit is 40%.
  • the content of Cr is more desirably 20% to 30%.
  • Ni is contained in at least 20% or more. Since the effect of increasing the amount is not obtained when Ni is contained in more than 55%, the upper limit is 55%.
  • the content of Ni is more preferably 28% to 45%.
  • Al is contained in at least 2% or more, and the upper limit is defined as 4%.
  • the content of Al is more desirably 2.5% to 3.8%.
  • C is contained in at least 0.3%, and the upper limit is 0.7%.
  • the content of C is more desirably 0.4% to 0.5%.
  • Si is contained in at least 0.1%, and is contained in the upper limit of 1.5%.
  • the content of Si is desirably 1.0% or less.
  • Mn is contained in the upper limit of 3.0%.
  • the content of Mn is more desirably 1.6% or less.
  • the rare earth element contained in the heat resistant alloy of the second embodiment according to the present invention is preferably at least one kind selected from the group consisting of Ce, La and Nd.
  • the rare earth element is contained in 0.005% or more, and the upper limit of 0.4%.
  • W and Mo at least one of W and Mo is contained, and when W is contained, the content is 0.5% or more, whereas when Mo is contained, the content is 0.1% or more.
  • W is 3% or less, and Mo is 2% or less. Even when both elements are contained, the total content is preferably 3% or less.
  • Ti and Zr are contained in 0.01% or more, and Nb is contained in 0.1% or more.
  • the upper limit is 0.6% for Ti and Zr, and 3.0% for Nb.
  • B may be contained as is necessary. Even when it added, the amount is more than 0% and 0.1% or less. The content of B is more preferably more than 0.01% and 0.1% or less.
  • the heat resistant alloy forming the cast body of the second embodiment according to the present invention contains the above components, and the remainder of Fe, and for increasing diffusion of Al and promoting generation of film of Al 2 O 3 , it preferably contains 25% or more of Fe. Further, the remainder of Fe may contain P, S and other impurities that are inevitably contained at the time of casting into an alloy, within the ranges that are generally allowable for this kind of alloy material.
  • the cast body forming the cast product of the second embodiment according to the present invention is casted to have the aforementioned composition by producing molten metal, and followed by mold centrifugal casting, stationary casting or the like.
  • a straight tube As a shape of the cast body, a straight tube, and a U-shaped tube with a bent portion formed by bending a straight tube, etc. are exemplified.
  • a straight tube the one having such inner diameter or length for which surface treatment by a polishing process or the like is difficult to be effected, is particularly suited, and as such a cast body, for example, a straight tube having an inner diameter of 40 mm or less and/or a length of 3000 mm or more can be exemplified. Further, so-called finishing processes such as an inner surface process and an inner surface honing may also be conducted as is necessary.
  • the aforementioned cast body is subjected to a surface treatment by an acid treatment for the objective site where it is to be in contact with a high temperature atmosphere during use of the product, and thus the surface roughness in the site is adjusted, and then subjected to a heating treatment in an oxidizing atmosphere.
  • the surface treatment is an acid treatment by an acid solution containing a polyhydric alcohol liquid.
  • the surface treatment by an acid treatment is preferably conducted for the entire objective site where it is to be in contact with a high temperature atmosphere during use of the product.
  • the acid treatment may be conducted only in the part out of reach of the polishing process, or in and around the bent portion of the U-shaped tube.
  • the acid treatment may be conducted so that the surface roughness (Ra) of the objective site is 0.05 ⁇ m to 2.5 ⁇ m. More desirably, the surface roughness (Ra) is 0.5 ⁇ m to 1.0 ⁇ m. As a result, it is possible to suppress generation of Cr oxide scale, and to form the alumina barrier layer containing Al 2 O 3 by the subsequent heat treatment more preferably.
  • the acid treatment can be achieved by dipping the objective site in an acid solution containing a polyhydric alcohol liquid for a predetermined time, or by applying an acid solution containing a polyhydric alcohol liquid to the objective site.
  • the corrosive liquid adhered to the objective site after the acid treatment is desirably washed out by water washing or the like.
  • polyhydric alcohol liquid polyhydric alcohols such as glycerol and glycol are exemplified.
  • the oxidizing power is too strong only by strong acid, and the surface of the objective site will be corroded too much to reversely make the surface rough.
  • a polyhydric alcohol liquid is added to the acid solution.
  • the polyhydric alcohol liquid it is possible to control or suppress the degree of oxidation or corrosion in the objective site by the acid solution, and to adjust the surface roughness.
  • the polyhydric alcohol liquid it is possible to suppress the oxidizing force and to facilitate adjustment of the surface roughness in comparison with the case of using monohydric alcohol.
  • a heat treatment is conducted in the same condition as described in the part ⁇ Heat treatment> in the first embodiment.
  • the cast body by subjecting the cast body to a surface treatment by an acid treatment in a site that is to be in contact with a high temperature atmosphere during use of the product, to adjust the surface roughness of the site, and then subjecting the site to a heating treatment in an oxidizing atmosphere, Al 2 O 3 is formed continuously as an alumina barrier layer on the surface of the cast product. As a result, it is possible to form an alumina barrier layer over the entire surface of the objective site of the cast body.
  • the thickness of the alumina barrier layer formed on the cast body is formed into 0.05 ⁇ m or more and 3 ⁇ m or less for effectively exerting a barrier function, and is preferably about 1 ⁇ m on average. More desirably, the thickness of the alumina barrier layer is 0.5 ⁇ m or more and 1.5 ⁇ m or less.
  • a cast body having the aforementioned composition of Cr—Ni—Al heat resistant alloy when a straight tube having small diameter and/or large length, and thus having a site for which a surface treatment by a polishing process of the like cannot be effected, is heated in an oxidizing atmosphere, the surface roughness is large and an alumina barrier layer is not formed in the site for which the surface treatment cannot be effected. Therefore, it is influenced by oxidization, cementation and so on from such a site.
  • the barrier layer formed on the surface of the straight tube, particularly on the ventral side of the bent portion can peel off due to strain or the like arising in the bent portion.
  • Cr oxide scale based on Cr 2 O 3 is dispersedly formed on the surface of the cast body, and is easy to peel off as described above, and at the time of peeling off, the alumina barrier layer beneath the same can peel off together.
  • the second embodiment according to the present invention by subjecting the objective site of the cast body to a surface treatment by an acid treatment, to adjust the surface roughness as described above, it is possible to form the alumina barrier layer stably over the entire objective site.
  • Cr oxide scale scattered on the alumina barrier layer is less than 20 area % of the product surface and the alumina barrier layer occupies 80 area % or more when the surface of the product is examined by SEM/EDX.
  • the alumina barrier layer covers 50% or more of the bent portion, and has a thickness of 0.05 ⁇ m or more by subjecting a straight tube to a bending process before acid treatment, and then conducting a treatment by acid containing the polyhydric alcohol liquid.
  • the third embodiment according to the present invention obtains a cast product in which a welded part is formed by a so-called “alumina barrier layer” containing Al 2 O 3 , by joining a first cast body and a second cast body made of a heat resistant alloy containing 15% or more of Cr and 20% or more of Ni, and 2 to 4% of Al by welding, and subjecting a welded part between the welded first cast body and the second cast body to a surface treatment, and then subjecting the welded part to a heat treatment.
  • alumina barrier layer containing Al 2 O 3
  • the contents of the components contained in the cast product of the third embodiment are identical to those in the second embodiment.
  • the first cast body and the second cast body forming the cast product of the third embodiment according to the present invention are casted to have the aforementioned composition by producing molten metal, followed by centrifugal casting, stationary casting or the like.
  • the obtained first cast body and second cast body may be joined by welding into a shape suited for the intended use.
  • edge preparation or the like may be conducted as is necessary.
  • the welding method and the composition of the welding electrode used at the time of welding are not limited, and as a method capable of welding the cast bodies of the present invention, TIG welding and arc welding can be recited.
  • a welded part including a heat influenced part and a molten metal part is formed in the joint portion regardless of whether a previous surface treatment is conducted. Residual stress and strain arise in this heat influenced part, and Cr migrates along the strain line of the heat influenced part, and Cr oxide is likely to be generated dominantly, and Al 2 O 3 is difficult to be generated.
  • a surface treatment is conducted on an objective site that is to be in contact with a high temperature atmosphere during use of the product, to adjust the surface roughness of the site, and then a heating treatment is conducted in an oxidizing atmosphere.
  • a polishing treatment can be exemplified. It is desired that the surface treatment is conducted on the entire objective site that is to be in contact with a high temperature atmosphere during use of the product. It is not necessary to treat the entire objective site concurrently, and the part other than the welded part may be previously subjected to a surface treatment or the like to adjust the surface roughness, and the surface treatment may be conducted only on the welded part or only on and around the welded part.
  • the surface treatment may be conducted so that the surface roughness (Ra) of the objective site is 0.05 ⁇ m to 2.5 ⁇ m. More desirably, the surface roughness (Ra) is 0.5 ⁇ m to 1.0 ⁇ m. The influence of the surface roughness (Ra) is described in the part ⁇ Surface treatment> in the first embodiment.
  • the surface treatment can be achieved by dipping the objective site in a corrosive liquid for a predetermined time, or by applying a corrosive liquid.
  • the acid used in the acid treatment may contain alcohol besides acid.
  • the corrosive liquid adhered to the objective site after the acid treatment is desirably washed out by water washing or the like.
  • a site that is to be in contact with a high temperature atmosphere during use of the product is subjected to a surface treatment, and the surface roughness of the site is adjusted, and then the site is subjected to a heating treatment in an oxidizing atmosphere, and thereby Al 2 O 3 is continuously formed as an alumina barrier layer on the surface continuing across the welded part of the cast product.
  • the alumina barrier layer is formed not only on the surface of the cast bodies, but also in the welded part including a heat influenced part arising in the abutting surface of the cast bodies by the welding.
  • the thickness of the alumina barrier layer formed on the cast bodies is 0.05 ⁇ m or more and 3 ⁇ m or less for effective exertion of barrier function, and is preferably about 1 ⁇ m on average. More desirably, the thickness of the alumina barrier layer is 0.5 ⁇ m or more and 1.5 ⁇ m or less.
  • an alumina barrier layer will not be formed particularly in the welded part having large surface roughness when the heating treatment is conducted in an oxidizing atmosphere without conducting a surface treatment after conducting the welding. Therefore, it is influenced by oxidation, cementation or the like from the welded part.
  • Cr oxide scale based on Cr 2 O 3 is dispersedly formed on the superficial surface of the cast bodies, and is easy to peel off as described above, and at the time of peeling off, the alumina barrier layer beneath the same can peel off together.
  • the third embodiment according to the present invention by adjusting the surface roughness by a surface treatment of a cast product after joining the cast bodies by welding and before formation of an alumina barrier layer by a heat treatment as described above, it is possible to form an alumina barrier layer stably in a welded part including a heat influenced part of the cast bodies arising by welding.
  • Cr oxide scale scattered on the alumina barrier layer is less than 20 area % of the product surface and the alumina barrier layer occupies 80 area % or more when the surface of the product is examined by SEM/EDX.
  • Molten metal was produced by atmospheric melting in a high frequency induction melting furnace, and specimen tubes having the alloy chemical compositions as shown in Table 1 below (outer diameter 59 mm, thickness 8 mm, length 3000 mm) were casted by centrifugal casting.
  • specimen Nos. 11 to 23 are inventive examples, and specimen Nos. 101 to 105 are comparative examples.
  • the comparative examples include specimen Nos. 101 to 104 which are comparative examples containing a larger amount of Ce than La in comparison with the alloy chemical composition of the present invention, and specimen No. 105 which is a comparative example in which the content of La is less than 80% with respect to the total amount of La and Ce.
  • a tensile test piece was prepared from a specimen tube in conformance with JIS Z 2201, and a ductility test was conducted. Concretely, the test piece was processed to have a parallel part diameter of 10 mm and a parallel part length of 50 mm, and ductility test was conducted according to the metal material tensile test method of JIS G 0567. The test was conducted at 1100° C.
  • Table 2 reveals that specimen Nos. 11 to No. 23 which are inventive examples are almost comparable with specimen Nos. 101 to No. 105 which are comparative examples.
  • the inventive example is about 10 times the comparative example.
  • Excellent elongation (high temperature tensile ductility) in specimen Nos. 11 to No. 23 which are inventive examples is attributed to the fact that the generation amount of Ni—La compounds such as Ni 2 La and Ni 3 La having excellent high temperature tensile ductility can be increased by making the content of La in the rare earth element 80% or more.
  • specimens 101 to 105 which are comparative examples are attributed to the fact that the generation amount of Ni—Ce compounds such as Ni 2 Ce and Ni 3 Ce is large due to a high content of Ce in the rare earth element, namely a content of La of less than 80%, and this causes high temperature brittleness.
  • specimen No. 18 containing 0.12% of La and 0.03% of Ce as the rare earth element shows elongation (high temperature tensile ductility) comparable with those in other inventive examples. This is because the generation amount of the Ni—Ce compounds can be controlled by making Ce 0.1% or less.
  • the cast product of the present invention is not only able to form a uniform alumina barrier layer on the entire surface of the cast body, and effectively prevent oxygen, carbon, nitrogen and the like from entering from external atmosphere, but also has excellent high temperature tensile ductility.
  • the specimen tubes were produced by centrifugal casting, however, similar results can be obtained by stationary casting.
  • Molten metal was produced by atmospheric melting in a high frequency induction melting furnace, and a specimen tube (outer diameter 59 mm, thickness 8 mm, length 3000 mm) containing C: 0.4 mass %, Si: 1.3 mass %, Mn: 1.1 mass %, Cr: 24.3 mass %, Ni: 34.7 mass %, Al: 3.36 mass %, rare earth element: 0.25 mass %, W: 2.9 mass %, Ti: 0.12 mass %, and the remainder of Fe and an inevitable impurity was casted by mold centrifugal casting.
  • Specimen Nos. 201 to 209 are inventive examples
  • specimen Nos. 311 to 312 are reference examples
  • specimen No. 421 is a comparative example.
  • specimen Nos. 201 to No. 209 which are inventive examples were dipped in an acid solution containing a polyhydric alcohol liquid for 3 minutes or for 10 minutes.
  • Specimen Nos. 311 and No. 312 which are reference examples were dipped in an acid solution not containing a polyhydric alcohol liquid in a similar manner.
  • inventive examples and reference examples subjected to an acid treatment were washed with water after the acid treatment.
  • Specimen No. 421 which is a comparative example was not subjected to an acid treatment.
  • Table 3 reveals that in specimen Nos. 201 to No. 209 which are inventive examples, surface roughness (Ra) is adjusted within the range of 0.42 ⁇ m to 0.74 ⁇ m by conduction of the acid treatment. Also, FIG. 1 to FIG. 7 which are surface photographs reveal that every specimen piece has surface glaze, and the scratch occurring by the skiving process is smoothed by the acid treatment by the acid solution containing a polyhydric alcohol liquid.
  • Specimen No. 311 and No. 312 which are reference examples dipped in an acid solution (aqua regia) not containing a polyhydric alcohol liquid have surface roughness (Ra) exceeding 1.0 ⁇ m, and the surface photographs thereof ( FIG. 8 and FIG. 9 ) reveal that the surface do not have glaze. This is because the surface is excessively corroded by corrosion by the treatment only with strong acid, and asperity occurs adversely.
  • Thickness of an alumina barrier layer was measured by a SEM (scanning electron microscope).
  • specimen Nos. 201 to No. 207, No. 311, No. 312 and No. 421 on which heat treatment was conducted surface photographing of the inner surface of the specimen piece and section SEM analysis were conducted.
  • section SEM analysis a specimen piece was plated with Ni, covered with a stainless sheet, and further coated with resin thereon.
  • FIG. 11 to FIG. 17 are surface photographs and FIG. 21 to FIG. 27 are section SEM photographs of specimen Nos. 201 to No. 207, and FIG. 18 to FIG. 20 are surface photographs and FIGS. 28 to 30 are section SEM photographs of specimen Nos. 311, No. 312 and No. 421.
  • Table 3 reveals that in any of specimen Nos. 201 to No. 209 which are inventive examples, the film thickness is 0.1 ⁇ m to 0.9 ⁇ m, and a desired alumina barrier layer is formed. Also FIG. 11 to FIG. 17 , and FIG. 21 to FIG. 27 reveal that a uniform alumina barrier layer is formed on the entire surface. This is because surface roughness (Ra) is adjusted by the acid solution containing a polyhydric alcohol liquid, and scratches and the like by skiving process are also smoothed.
  • Ra surface roughness
  • the low area percentage of film in specimen No. 207 in which the polyhydric alcohol liquid is 60% is attributable to the fact that the oxidizing power of the acid solution is decreased as a result of increase in the polyhydric alcohol liquid, and sufficient adjustment of surface roughness (Ra) by corrosion cannot be achieved.
  • polyhydric alcohol liquid contained in the acid solution is preferably more than 10% and 40% or less.
  • specimen Nos. 311 and No. 312 which are reference examples, formation of a film is little observed as shown in Table 3, FIG. 18 and FIG. 19 . This is because as shown in FIG. 28 and FIG. 29 , as a result of conducting an acid treatment only by strong acid, the surface of the base material is rough, and formation of an alumina barrier layer is inhibited.
  • specimen No. 421 which is a comparative example, as shown in Table 3, FIG. 20 and FIG. 30 , surface roughness (Ra) is preferable, and film is formed, however, it can be realized that the formed film is not continuous. This is because formation of the alumina barrier layer is inhibited by scratches occurring by a skiving process.
  • the cast product of the present invention since the cast product of the present invention has high ductility and a uniform alumina barrier layer generated on the surface of the cast body, it is resistant to peeling even when it is exposed to repeated heating and cooling cycles, and since the alumina barrier layer is tight, excellent repetitive oxidation resistance is exerted in use in a high temperature atmosphere, and entry of oxygen, carbon, nitrogen and the like from the external atmosphere is effectively prevented, and excellent repetitive oxidation resistance at high temperature, cementation resistance, nitriding resistance, corrosion resistance and so on can be maintained for a long term.
  • the present invention may be applied to cast products for which a horning process or the like cannot be effected, such as a long cast product and a cast product subjected to a bending process, and as a result, a preferable alumina barrier layer can be formed.
  • Molten metal was produced by atmospheric melting in a high frequency induction melting furnace, and respectively two tube bodies (outer diameter 59 mm, thickness 8 mm, length 3000 mm) having alloy chemical compositions as recited in Table 4 below were casted by mold centrifugal casting, and edge preparation was conducted in one side of the tube bodies, and tube bodies having the same composition and are to be a pair were joined by abutment welding.
  • the obtained specimen tubes include specimen tubes No. 501 to No. 508 which are examples of the present invention, and specimen tubes No. 611 to No. 613 which are comparative examples. More concretely, the comparative examples include specimen tube No. 611 which is a comparative example containing more Al than that in the alloy chemical composition of the present invention, specimen tube No. 612 which is a comparative example containing more Ni than that in the alloy chemical composition of the present invention, and specimen tube No. 613 which is a comparative example having the alloy chemical composition falling within the present invention but not subjected to a surface treatment in the welded part.
  • skiving which is rough processing was conducted in the region extending about 20 mm to 40 mm in the width direction centered at the welded part in the inner side of the tube.
  • specimen tube No. 504 which is an inventive example
  • specimen tube No. 613 which is a comparative example
  • photographs of the specimen tubes cut along the axial direction are respectively shown in FIG. 31 and FIG. 32 .
  • specimen No. 504 which is an inventive example has glaze in the welded part, and has reduced asperity of the welded part as a result of the surface treatment.
  • Thickness of an alumina barrier layer for the welded part surface of a specimen piece was measured by a SEM (scanning electron microscope).
  • the specimen in which an alumina barrier layer was not generated, and the specimen in which the site having a thickness of less than 0.05 ⁇ m (including the thickness of zero) appeared intermittently in a part of the alumina barrier layer, are marked with the character N (No) in Table 5.
  • Area percentage of Al 2 O 3 to the surface of the welded part of the specimen piece was determined by using a SEM/EDX (scanning analytical electron microscope) measurement tester. Measurement was conducted for a region of 1.35 mm ⁇ 1 mm on the surface of the welded part of the specimen piece, and distribution condition of Al was surface analyzed, and the distribution quantity was converted to area percentage.
  • a tensile test piece was prepared from a specimen tube in conformance with JIS 22201, and a ductility test was conducted.
  • the test piece was processed to have a parallel part diameter of 10 mm and a parallel part length of 50 mm including the welded part, and ductility test was conducted according to the metal material tensile test method of JIS 22241. The test was conducted at room temperature because difference arises more clearly, than as it is conducted at high temperature.
  • Table 5 reveals that specimen tubes No. 501 to No. 508 which are inventive examples show better film thickness of the alumina barrier layer and area percentage in comparison with specimen tubes No. 611 to No. 613 which are comparative examples.
  • any film thickness falls within the preferred range of 0.05 ⁇ m or more and 3 ⁇ m or less. It is also revealed that the tensile ductility is sufficient.
  • specimen tubes No. 507 and No. 508 are inferior in film thickness and area percentage to other inventive examples, and this is attributed to the fact that surface roughness by a surface treatment of specimen tube No. 507 is large, and surface roughness by a surface treatment of specimen tube No. 508 is too fine. Therefore, it can be found that the surface treatment conducted on the welded part preferably makes the surface roughness (Ra) of 0.05 ⁇ m to 2.5 ⁇ m for making the alumina barrier layer of the welded part 80 area % or more.
  • specimen tube No. 611 is inferior in tensile ductility although a preferred alumina barrier layer is formed. This is because the content of Al in the alloy chemical composition exceeds 4%. Therefore, it is revealed that the content of Al is preferably 4% or less.
  • specimen tubes No. 612 and No. 613 a sufficient alumina barrier layer is not formed.
  • the content of Ni in the alloy chemical composition is smaller than 18%, and as a result the content of Fe is relatively large, and Cr—Fe—Mn oxide is more likely to be generated on the surface of the cast body, so that generation of an alumina barrier layer is inhibited.
  • specimen pieces obtained from specimen tube No. 504 which is an example of the present invention, and specimen tube No. 613 which is a comparative example photographs of the section perpendicular to the welded part were taken, and section SEM analysis was conducted.
  • section SEM analysis the specimen piece was plated with Ni, covered with a stainless steel sheet, and further coated with resin thereon.
  • an alumina barrier layer having a film thickness of 0.5 ⁇ m is uniformly formed on the surface of the base material.
  • the asperity of the surface is significant, and an alumina barrier layer is not successfully formed.
  • a uniform alumina barrier layer can be formed on the entire surface of the cast body including a welded part by conducting a heat treatment after subjecting the welded part to a surface treatment, so that entry of oxygen, carbon, nitrogen and the like from the external atmosphere is effectively inhibited, and the cast body as a whole including the welded part is able to keep the excellent repeated oxidation resistance at high temperature, cementation resistance, nitriding resistance, corrosion resistance and the like for a long term.
  • the present invention is useful as a cast product having an alumina barrier layer and a method for producing the same.

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US11136655B2 (en) 2017-11-06 2021-10-05 Kubota Corporation Heat-resistant alloy, and reaction tube
US11155756B2 (en) 2014-12-16 2021-10-26 Exxonmobil Chemical Patents Inc. Pyrolysis furnace tubes
US11261506B2 (en) * 2017-02-28 2022-03-01 Saint-Gobain Seva Alloy for a fibre-forming plate
US20220251690A1 (en) * 2021-01-29 2022-08-11 Ut-Battelle, Llc Creep and corrosion-resistant cast alumina-forming alloys for high temperature service in industrial and petrochemical applications
WO2023047142A1 (fr) * 2021-09-27 2023-03-30 Alloyed Limited Acier inoxydable austénitique
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EP2829628B1 (fr) 2020-03-04

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