WO2013018320A1 - 燃料電池セパレータ用ステンレス鋼 - Google Patents
燃料電池セパレータ用ステンレス鋼 Download PDFInfo
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- WO2013018320A1 WO2013018320A1 PCT/JP2012/004736 JP2012004736W WO2013018320A1 WO 2013018320 A1 WO2013018320 A1 WO 2013018320A1 JP 2012004736 W JP2012004736 W JP 2012004736W WO 2013018320 A1 WO2013018320 A1 WO 2013018320A1
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
- H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
- H01M8/0204—Non-porous and characterised by the material
- H01M8/0206—Metals or alloys
- H01M8/0208—Alloys
- H01M8/021—Alloys based on iron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- 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
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- 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
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- 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
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- 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
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- 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
- C23C22/00—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C22/05—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using aqueous solutions
- C23C22/06—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using aqueous solutions using aqueous acidic solutions with pH less than 6
- C23C22/34—Chemical surface treatment of metallic material by reaction of the surface with a reactive liquid, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using aqueous solutions using aqueous acidic solutions with pH less than 6 containing fluorides or complex fluorides
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- C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
- C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
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- 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
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
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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
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
- C23G1/086—Iron or steel solutions containing HF
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- C25F—PROCESSES FOR THE ELECTROLYTIC REMOVAL OF MATERIALS FROM OBJECTS; APPARATUS THEREFOR
- C25F1/00—Electrolytic cleaning, degreasing, pickling or descaling
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- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25F—PROCESSES FOR THE ELECTROLYTIC REMOVAL OF MATERIALS FROM OBJECTS; APPARATUS THEREFOR
- C25F1/00—Electrolytic cleaning, degreasing, pickling or descaling
- C25F1/02—Pickling; Descaling
- C25F1/04—Pickling; Descaling in solution
- C25F1/06—Iron or steel
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/10—Fuel cells with solid electrolytes
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- 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
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/30—Hydrogen technology
- Y02E60/50—Fuel cells
Definitions
- the present invention relates to a stainless steel for a fuel cell separator (corresponding to corrosion resistance (corrosion resistance) and contact resistance resistance characteristics and ability to maintain contact resistance).
- This fuel cell reacts hydrogen and oxygen (reaction (of hydrogen with oxygen) to generate electricity, and its basic structure has a sandwich-like structure (a sandwich structure), and an electrolyte membrane ( an electrolyte membrane, ion-exchange membrane, two electrodes (a fuel electrode and an air electrode), hydrogen and oxygen (air) diffusion layer, and two separators (separators).
- an electrolyte membrane an electrolyte membrane, ion-exchange membrane, two electrodes (a fuel electrode and an air electrode), hydrogen and oxygen (air) diffusion layer, and two separators (separators).
- phosphoric acid form phosphoric acid fuel cell
- molten carbonate form molten sodium carbonate fuel cell
- solid oxide form solid oxide fuel cell
- alkaline form alkaline fuel cell
- solid Polymer type solid-polymer fuel-cell
- the polymer electrolyte fuel cell is (1) the operating temperature is about 80 ° C. is much lower than the molten carbonate type and phosphoric acid type fuel cells, etc. It has features such as light weight and small size, (3) quick start-up (a short transient time), fuel efficiency (fuel efficiency), and high output density (output density). For this reason, polymer electrolyte fuel cells are attracting the most attention today for use as electric power sources for electric vehicles (vehicles) and small distributed power sources (compacts, distributed power sources, for homes). Is one of the fuel cells.
- the polymer electrolyte fuel cell is based on the principle of extracting electricity from hydrogen and oxygen through a polymer membrane, and the structure is shown in Fig. 1 (b).
- MEA 10Membrane-Electrode Assembly, thickness 10 to several 100 ⁇ m
- the gas diffusion layer is often integrated with the MEA.
- Several tens to hundreds of single cells are connected in series to form a fuel cell stack (form a fuel cell stack).
- the separator has (1) conductors that carry generated electrons (conductors carrying electrons generated), (2) oxygen (air) and hydrogen channels ( channels for oxy (air) and hydrogen) (air channel 6 and hydrogen channel 7 in Fig. 1 respectively) and (3) generated water and exhaust gas discharge channels (channels for water and exhaust gas) (Fig. 1 respectively) Functions as the air flow path 6 and the hydrogen flow path 7) are required.
- separators having excellent durability and electrical conductivity.
- separators separators using carbonaceous materials such as graphite are provided.
- various materials such as titanium alloys are being studied.
- this carbon separator has the disadvantages that it is easily damaged by impact, is difficult to make compact, and the processing cost for forming the flow path is high.
- the cost problem is the biggest obstacle to the spread of fuel cells. Therefore, there is an attempt to apply a metal material, particularly stainless steel, instead of the carbon material.
- Patent Document 1 discloses a technique in which a metal that easily forms a passive film is used as a separator.
- a metal that easily forms a passive film causes an increase in contact resistance, leading to a decrease in power generation efficiency.
- these metal materials have problems to be improved such as a contact resistance larger than that of the carbon material and inferior in corrosion resistance.
- Patent Document 2 discloses a technique for reducing contact resistance and ensuring high output by applying gold plating to the surface of a metal separator such as SUS304 (a metallic separator plated with gold). It is disclosed. However, it is difficult to prevent the occurrence of pinholes with thin gold plating, and conversely, thick gold plating costs high.
- Patent Document 3 discloses a method for obtaining a separator having improved electrical conductivity by dispersing carbon powders in a ferritic stainless steel substrate.
- the surface treatment of the separator requires a considerable cost.
- the separator subjected to the surface treatment has a problem that the corrosion resistance (corrosion resistance) is remarkably lowered when scratches or the like are generated during assembly.
- Patent Document 4 is a stainless steel plate characterized in that the average interval between the local peaks of the surface roughness curve is 0.3 ⁇ m or less, whereby the contact resistance can be reduced to 20 m ⁇ ⁇ cm 2 or less.
- This technology has made it possible to provide fuel cell separator materials made of stainless steel.
- further improvements in contact resistance characteristics are desirable in fuel cell design, and a contact resistance of 10 m ⁇ ⁇ cm 2 or less is required to be stable. It is.
- the contact resistance is likely to increase due to surface deterioration in the positive electrode (air electrode) exposed to a high potential, so that the contact resistance of 10 m ⁇ ⁇ cm 2 or less can be maintained for a long time in the use environment even in the separator. is necessary.
- the present invention has been made in view of such circumstances, and an object thereof is to provide a stainless steel for a fuel cell separator excellent in contact resistance characteristics and contact resistance maintaining ability.
- the present inventors have intensively studied in order to improve the contact resistance characteristics in the stainless steel for fuel cell separator and to maintain the contact resistance for a long time.
- the steel surface contains fluorine and the peak intensities of Cr and Fe when measured by photoelectron spectroscopy (X-ray electro Photoelectron tro Spectroscopy) (hereinafter sometimes referred to as XPS)
- XPS photoelectron spectroscopy
- the present invention is based on the above findings, and features are as follows. [1] Mass%, C: 0.03% or less, Si: 1.0% or less, Mn: 1.0% or less, S: 0.01% or less, P: 0.05% or less, Al: 0.20% or less, N: 0.03 Or less, Cr: 16-40%, Ni: 20% or less, Cu: 0.6% or less, Mo: 2.5% or less, one or more types of stainless steel with the balance of Fe and inevitable impurities A stainless steel for fuel cell separators, wherein F is detected when the surface of the stainless steel is measured by photoelectron spectroscopy, and the following is satisfied.
- the stainless steel for fuel cell separators which was excellent in the contact resistance characteristic and excellent in the practicality which can maintain the contact resistance over a long time is obtained.
- the stainless steel of the present invention as a separator instead of the conventional expensive carbon or gold plating, an inexpensive fuel cell can be provided and the spread of the fuel cell can be promoted.
- the stainless steel used as a material is not particularly limited in the steel type or the like as long as it has the corrosion resistance required under the operating environment of the fuel cell.
- it is necessary to contain 16% by mass or more of Cr.
- the Cr content is less than 16% by mass, the separator cannot be used for a long time.
- it is 18 mass% or more.
- the toughness may decrease due to precipitation of the ⁇ phase, so the Cr content is 40% by mass or less.
- C 0.03% or less C reacts with Cr in the stainless steel and precipitates as Cr carbide in the grain boundary (precipitate chromium carbonitride in the grain boundary), resulting in a decrease in corrosion resistance. Therefore, the smaller the C content, the better. If C is 0.03% or less, the corrosion resistance is not significantly reduced. Preferably it is 0.015% or less.
- Si 1.0% or less Si is an effective element for deoxidation, and is added at the melting stage of stainless steel. However, if excessively contained, the stainless steel hardens (causes hardening of the stainless steel sheet) and the ductility decreases (decreased ductility). More preferably, it is 0.01% or more and 0.6% or less.
- Mn 1.0% or less Mn combines with inevitably mixed S, has the effect of reducing S dissolved in stainless steel, suppresses segregation of sulfur at the grain boundary, and performs hot rolling. It is an effective element for preventing cracking of the steel sheet during hot rolling. However, even if added over 1.0%, there is almost no increase in the effect of addition. On the other hand, an excessive addition causes an increase in cost. Therefore, Mn is 1.0% or less.
- S 0.01% or less S is an element that lowers the corrosion resistance by binding to Mn to form MnS, and is preferably lower. If it is 0.01% or less, the corrosion resistance will not be significantly reduced. Therefore, S is set to 0.01% or less.
- P 0.05% or less P lowers the ductility because it lowers the ductility. However, if it is 0.05% or less, the ductility is not significantly reduced. Therefore, P is 0.05% or less.
- Al 0.20% or less
- Al is an element used as a deoxidizing element.
- Al is 0.20% or less.
- N 0.03% or less N is an element effective for suppressing local corrosion such as crevice corrosion of stainless steel. However, if added over 0.03%, it takes a long time to add N in the melting stage of the stainless steel, resulting in a decrease in productivity and a decrease in the formability of the steel. Therefore, N is set to 0.03% or less.
- Ni 20% or less
- Cu 0.6% or less
- Mo 2.5% or less
- Ni 20% or less
- Ni is an element that stabilizes the austenitic phase, and is added when producing austenitic stainless steel. At this time, if the Ni content exceeds 20%, excessive consumption of Ni causes an increase in cost. Therefore, Ni is 20% or less.
- Cu: 0.6% or less Cu is an element effective for improving the corrosion resistance of stainless steel. However, if added over 0.6%, hot workability deteriorates, leading to a decrease in productivity, and adding Cu excessively increases the cost. Therefore, Cu is made 0.6% or less.
- Mo 2.5% or less
- Mo is an element effective in suppressing local corrosion such as crevice corrosion of stainless steel. However, if added over 2.5%, the stainless steel becomes extremely brittle and productivity is lowered, and excessive consumption of Mo leads to an increase in cost. Therefore, Mo is 2.5% or less.
- one or more of Nb, Ti, and Zr can be added to improve intergranular corrosion resistance in addition to the elements described above. However, if it exceeds 1.0% in total, ductility is reduced. In addition, the cost increases due to the addition of elements. Therefore, when added, Ti, Nb, and Zr are preferably 1.0% or less in total.
- the balance is Fe and inevitable impurities.
- the stainless steel of the present invention is characterized by detecting F when the surface is measured by photoelectron spectroscopy and satisfying the following.
- the term “other than the metal form (Cr + Fe)” refers to the total atomic concentration of Cr and Fe other than the metal form calculated from the result of separating the Cr and Fe peaks into the metal peak and the peak other than the metal peak.
- the metal form (Cr + Fe) is the sum of atomic concentrations of Cr and Fe in a metal form calculated from the result of separating the Cr and Fe peaks into a metal peak and a peak other than the metal peak.
- Fig. 2 shows a wide scan spectrum in XPS measurement when the surface of the stainless steel of the present invention is measured by XPS. From FIG. 2, a value of 0.1 at% or more is obtained in the quantification by the relative sensitivity coefficient (Relative Sensitivity Factor), and F can be clearly detected.
- Relative Sensitivity Factor Relative Sensitivity Factor
- Fig. 3 shows the 2p spectrum of Fe by XPS
- Fig. 4 shows the 2p spectrum of Cr. 3 and 4, it can be seen that the peak is separated into a peak other than metal and a peak of metal.
- the metal peak is detected in the portion with the lowest binding energy, and can be distinguished from the peak other than the metal (for example, compound state). Therefore, the peak other than the metal and the peak of the metal can be separated and the ratio can be obtained.
- Cr and Fe were quantified by relative sensitivity coefficient (atomic concentration), and the total of atomic concentrations of Cr and Fe obtained from the film using the results of separating each peak by peak separation, that is, other than metals
- the total atomic concentration of Cr and Fe in the form and the total atomic concentration of Cr and Fe obtained from the metal part, that is, the ratio of the total atomic concentration of Cr and Fe in the metallic form was calculated.
- the durability test was done, the contact resistance value before and after the test was measured, and the increase was calculated. In the durability test, a sample was kept for 24 hours in a pH 3 sulfuric acid solution under conditions of 800 mVvs SHE and a temperature of 80 ° C.
- Figure 5 shows the total atomic concentration of Cr and Fe in the non-metal form and the Cr and Fe in the metal form when the surface of stainless steel with F detected when the surface was measured by photoelectron spectroscopy was measured by XPS. It is a figure which shows the relationship of the ratio of total atomic concentration, ie, other than a metal form (Cr + Fe) / metal form (Cr + Fe), and the contact resistance value increase before and behind a durability test. From FIG. 5, it can be seen that when F is detected on the surface and there is more than a certain value other than the metal form (Cr + Fe) / metal form (Cr + Fe), the increase in the contact resistance value is small. As can be seen from FIG.
- the non-metal form (Cr + Fe) / metal form (Cr + Fe) have a good relationship with the increase in contact resistance, and the increase in contact resistance is 10 m ⁇ ⁇ cm 2 (20 kgf) as a measure of durability in the durability test. / Cm 2 ) or less to achieve non-metal form (Cr + Fe) / metal form (Cr + Fe) of 4.0 or more and 30 m ⁇ ⁇ cm 2 (20 kgf / cm 2 ) or less to 3.0 or more You can see that.
- Non-metal form (Cr + Fe) / Metal form (Cr + Fe) is set to 3.0 or more to increase the contact resistance to 30 m ⁇ ⁇ cm 2 (20 kgf / cm 2 ) or less, and the contact resistance before the durability test is 10 m ⁇ . • Can be 2 cm or less.
- metal form (Cr + Fe) / Metal form (Cr + Fe) ⁇ 3.0 Preferably, (Cr + Fe) / metal form (Cr + Fe) ⁇ 4.0.
- Separation of a peak in a form other than a metal and a peak in a metal form can be performed by a peak fitting method by a least square method using a Gaussian type peak by removing a spectral background by the Sherly method.
- hydrofluoric acid immersion treatment or the like can be used as a method for imparting F to the surface.
- other than the metal form (Cr + Fe) / metal form (Cr + Fe) can be within the scope of the present invention by controlling the treatment conditions such as the acid dipping treatment after annealing.
- the treatment time and the temperature of the treatment liquid can be changed to be within the scope of the present invention.
- by increasing the treatment time it is possible to increase the non-metal form (Cr + Fe) / metal form (Cr + Fe).
- the method for producing the stainless steel for a fuel cell separator of the present invention is not particularly limited, and may be a conventionally known method. Preferred production conditions are as follows.
- a steel slab adjusted to a suitable component composition is heated to a temperature of 1100 ° C or higher, hot-rolled, annealed at a temperature of 800-1100 ° C, and then cold-rolled and annealed repeatedly to obtain stainless steel. .
- the thickness of the obtained stainless steel plate is preferably about 0.02 to 0.8 mm.
- pretreatment electrolytic treatment or acid immersion
- acid treatment As an example of the electrolysis conditions, a method can be used in a sulfuric acid bath of 3% H 2 SO 4 at 2 A / dm 2 at 55 ° C. for 30 seconds.
- a method of immersing in a mixed solution of 5% hydrofluoric acid and 1% nitric acid at 55 ° C. for 40 seconds to 120 seconds can be employed.
- the electrolytic treatment was performed in the bath shown in Table 2, with the solution temperature being 55 ° C., the current density being 2 A / dm 2 , and the treatment time being 30 seconds.
- the solution temperature was 55 ° C. and the treatment time was 30 seconds.
- the acid treatment was performed using the solutions shown in Table 2, the bath temperature, and the time.
- the contact resistance was measured and the element present on the outermost surface was evaluated by XPS. Further, a durability test was performed, and the contact resistance was measured in the same manner as before the durability test, thereby obtaining an increase in contact resistance. In the durability test, the sample was kept in a sulfuric acid solution of pH 3 under conditions of 800 mVvs SHE and 80 ° C. for 24 hours.
- the contact resistance was measured by using a carbon paper CP120 manufactured by Toray Industries, Inc., contacting the carbon paper CP120 with steel, and applying a load of 20 kGf / cm 2 .
- AXIS-HS manufactured by KRATOS was used for XPS measurement. Measurement was performed using a monochromatized AIK ⁇ x-ray source, and the main component was quantified (atomic%) using the relative sensitivity coefficient attached to the device. From the results, F was quantified, and 2p of Cr and Fe was separated into metal peaks and other peaks, and information related to the film thickness was obtained by taking the ratio.
- the contact resistance is 10 m ⁇ ⁇ cm 2 or less and the contact resistance increase is 30 m ⁇ ⁇ cm You can see that it is 2 or less.
- the contact resistance increase is 10 m ⁇ ⁇ cm 2 or less, and the contact resistance maintaining characteristics are further improved. I can see that
- Example 1 Of the stainless steel plates having a thickness of 0.2 mm used in Example 1, steel numbers 2 and 3 in Table 1 were used.
- electrolytic treatment was performed in a 3% sulfuric acid solution.
- the solution temperature was 55 ° C.
- the current density was 2 A / dm 2
- the treatment time was 30 seconds.
- the acid treatment was performed using a mixed solution of 5% hydrofluoric acid and 1% nitric acid for Steel 2 and a 5% hydrofluoric acid solution for Steel 3.
- the temperature of the acid solution was 55 ° C., and the immersion time was 40 to 120 seconds.
- a sample not immersed in acid was also prepared.
- XPS measurement was performed on the surface of the obtained sample, and the presence or absence of F and the ratio of other than metal form (Cr + Fe) / metal form (Cr + Fe) were determined, and contact resistance was measured. Further, a durability test was performed, and the contact resistance was measured in the same manner as before the durability test, thereby obtaining an increase in contact resistance. These measurement and data analysis methods are the same as in Example 1. In the durability test, 0.1 ppm of F ions was added to a pH 3 sulfuric acid solution, and the sample was held for 20 hours under conditions of 800 mVvs SHE and 80 ° C.
- the contact resistance before the durability test is as low as 10 m ⁇ ⁇ cm 2 or less, and the increase in contact resistance after the durability test is 30 m ⁇ ⁇ cm 2 or less.
- test Nos. 3, 4 and 8 in which F is detected and the metal form (Cr + Fe) / metal form (Cr + Fe) is 3.5 or more the increase in contact resistance after the durability test is 10 m ⁇ ⁇ cm 2 or less, especially 4.0 or more Test Nos.
- Test No1 has a metal form other than the metal form (Cr + Fe) / metal form (Cr + Fe) of 3.0, but does not contain F and has high contact resistance before the test (therefore, the durability test is not conducted).
- Test Nos. 2 and 6 contain F, but the non-metal form (Cr + Fe) / metal form (Cr + Fe) is less than 3.0, and the contact resistance before the test and the increase in the contact resistance after the endurance test are both large and perform well. You can see that they are inferior
Abstract
Description
さらに、燃料電池では、高電位に晒される正極(空気極)において、表面の劣化により接触抵抗が増加しやすく、そのため、セパレータにおいても接触抵抗10mΩ・cm2以下が使用環境下で長く維持できることが必要である。
[1]質量%(mass%)で、C:0.03%以下、Si:1.0%以下、Mn:1.0%以下、S:0.01%以下、P:0.05%以下、Al:0.20%以下、N:0.03%以下、Cr:16~40%を含み、Ni:20%以下、Cu:0.6%以下、Mo:2.5%以下の一種以上を含有し、残部がFe および不可避的不純物からなるステンレス鋼であって、該ステンレス鋼の表面を光電子分光法により測定した場合に、Fを検出し、かつ、下記を満足することを特徴とする燃料電池セパレータ用ステンレス鋼。
金属形態以外(Cr+Fe)/金属形態(Cr+Fe)≧3.0
ただし、前記金属形態以外(Cr+Fe)とは、CrおよびFeのピークを金属ピークと金属ピーク以外のピークに分離した結果から算出される金属以外の形態のCrとFeの原子濃度(atomic concentration)の合計である。前記金属形態(Cr+Fe)とは、CrおよびFeのピークを金属ピークと金属ピーク以外のピークに分離した結果から算出される金属形態のCrとFeの原子濃度の合計である。
[2]前記ステンレス鋼が、さらに、質量%で、Nb、Ti、Zrの一種以上を合計で1.0%以下を含有することを特徴とする前記[1]に記載の燃料電池セパレータ用ステンレス鋼。
従来の高価なカーボンや金めっきに代わり、本発明のステンレス鋼をセパレータとして用いることで、安価な燃料電池を提供でき、燃料電池の普及を促進させることが可能となる。
Cは、ステンレス鋼中のCrと反応し、粒界にCr炭化物として析出する(precipitate chromium carbonitride in the grain boundary)ため、耐食性の低下をもたらす。したがって、Cの含有量は少ないほど好ましく、Cが0.03%以下であれば、耐食性を著しく低下させることはない。好ましくは 0.015%以下である。
Siは、脱酸のために有効な元素であり、ステンレス鋼の溶製段階で添加される。しかし過剰に含有させるとステンレス鋼が硬質化(causes hardening of the stainless steel sheet)し、延性が低下する(decreased ductility)ので、1.0%以下とする。さらに好ましくは、0.01%以上0.6%以下である。
Mnは、不可避的に混入したSと結合し、ステンレス鋼に固溶したSを低減する効果を有し、Sの粒界偏析を抑制(suppresses segregation of sulfur at the grain boundary)し、熱間圧延時の割れを防止する(prevents cracking of the steel sheet during hot rolling)のに有効な元素である。しかし、1.0%を超えて添加しても添加する効果の増加はほとんどない。かえって、過剰に添加することによってコストの上昇を招く。よって、Mnは1.0%以下とする。
SはMnと結合しMnSを形成することで耐食性を低下させる元素であり低い方が好ましい。0.01%以下であれば耐食性を著しく低下させることはない。よって、Sは0.01%以下とする。
Pは延性の低下をもたらすため、低いほうが望ましいが、0.05%以下であれば延性を著しく低下させることはない。よって、Pは0.05%以下とする。
Alは、脱酸元素として用いられる元素である。一方で、過剰に含有すると延性の低下をもたらす。よって、Alは0.20%以下とする。
Nは、ステンレス鋼の隙間腐食等の局部腐食を抑制するのに有効な元素である。しかし、 0.03%を超えて添加すると、ステンレス鋼の溶製段階でNを添加するために長時間を要するので生産性の低下を招くとともに、鋼の成形性が低下する。したがってNは、0.03%以下とする。
Ni:20%以下
Niは、オーステナイト相を安定化させる元素であり、オーステナイト系ステンレスを製造する場合に添加する。その際、Ni含有量が20%を超えると、Niを過剰に消費することによってコストの上昇を招く。したがってNiは、20%以下とする。
Cu:0.6%以下
Cuは、ステンレス鋼の耐食性を改善するのに有効な元素である。しかし、0.6%を超えて添加すると、熱間加工性が劣化し、生産性の低下を招くばかりでなく、Cuを過剰に添加することによってコストの上昇を招く。したがってCuは、0.6%以下とする。
Mo:2.5%以下
Moは、ステンレス鋼の隙間腐食等(crevice corrosion)の局部腐食を抑制するのに有効な元素である。しかし、2.5%を超えて添加すると、ステンレス鋼が著しく脆化して生産性が低下するとともに、Moを過剰に消費することによってコストの上昇を招く。したがってMoは、2.5%以下とする。
本発明では、上記した元素の他に、耐粒界腐食性向上のためにNb、Ti、Zrの一種以上を添加することができる。しかし、合計で1.0%を超えた場合、延性の低下を招く。また、元素添加によるコスト上昇をきたす。したがって、添加する場合は、Ti、Nb、Zrを合計で 1.0%以下が好ましい。
本発明のステンレス鋼は、表面を光電子分光法により測定した場合に、Fを検出し、かつ、下記を満足することを特徴とする。
金属形態以外(Cr+Fe)/金属形態(Cr+Fe)≧3.0
ただし、前記金属形態以外(Cr+Fe)とは、CrおよびFeのピークを金属ピークと金属ピーク以外のピークに分離した結果から算出される金属形態以外のCrとFeの原子濃度の合計である。前記金属形態(Cr+Fe)とは、CrおよびFeのピークを金属ピークと金属ピーク以外のピークに分離した結果から算出される金属形態のCrとFeの原子濃度の合計である。
金属形態以外(Cr+Fe)/金属形態(Cr+Fe)≧3.0
なお、好ましくは、(Cr+Fe)/金属形態(Cr+Fe)≧4.0である。
なお、金属以外の形態のピークと金属形態のピークの分離は、Sherly法によりスペクトルのバックグラウンドを除去し、ガウシアン型のピークを用いた最小二乗法によるピークフィッティング法により行うことができる。
酸処理の一例としては、5%フッ酸と1%硝酸の混合溶液に、55℃で、40秒~120秒浸漬する方法を採用することができる。
引き続き、焼鈍を施し、表2に示す条件で前処理(電解処理もしくは酸浸漬)、酸洗溶液に浸漬する酸処理を行った。なお、電解処理は表2に示す浴にて、溶液温度は55℃、電流密度は2A/dm2、処理時間は30秒の条件で行い、前処理としての酸浸漬は表2に示す溶液にて溶液温度は55℃、処理時間は30秒の条件で行った。また、酸処理は表2に示す溶液および浴温度、時間で行った。
以上により得られたステンレス鋼に対して、接触抵抗を測定するとともに、XPSによる測定を行い最表面に存在する元素を評価した。さらに耐久性試験を行い、耐久性試験前と同様に接触抵抗を測定することで、接触抵抗増加分を求めた。なお、耐久性試験は、pH 3の硫酸溶液中に800mVvs SHE、80℃の条件で試料を24時間保持した。
なお、耐久試験前の段階で接触抵抗が10mΩ・cm2以下とならなかったものについては、金属形態以外(Cr+Fe)/金属形態(Cr+Fe)および耐久試験後の接触抵抗の測定は行わなかった。
以上により得られた結果を表3に示す。
2 ガス拡散層
3 ガス拡散層
4 セパレータ
5 セパレータ
6 空気流路
7 水素流路
Claims (2)
- 質量%で、C:0.03%以下、Si:1.0%以下、Mn:1.0%以下、S:0.01%以下、P:0.05%以下、Al:0.20%以下、N:0.03%以下、Cr:16~40%を含み、Ni:20%以下、Cu:0.6%以下、Mo:2.5%以下の一種以上を含有し、残部がFe および不可避的不純物からなるステンレス鋼であって、
該ステンレス鋼の表面を光電子分光法により測定した場合に、
Fを検出し、かつ、下記を満足することを特徴とする燃料電池セパレータ用ステンレス鋼。
金属形態以外(Cr+Fe)/金属形態(Cr+Fe)≧3.0
ただし、前記金属形態以外(Cr+Fe)とは、CrおよびFeのピークを金属ピークと金属ピーク以外のピークに分離した結果から算出される金属以外の形態のCrとFeの原子濃度の合計であり、前記金属形態(Cr+Fe)とは、CrおよびFeのピークを金属ピークと金属ピーク以外のピークに分離した結果から算出される金属形態のCrとFeの原子濃度の合計である。 - 前記ステンレス鋼が、さらに、質量%で、Nb、Ti、Zrの一種以上を合計で1.0%以下を含有することを特徴とする請求項1に記載の燃料電池セパレータ用ステンレス鋼。
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Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2021006099A1 (ja) * | 2019-07-09 | 2021-01-14 | Jfeスチール株式会社 | 硫化物系固体電池の集電体用のフェライト系ステンレス鋼板およびその製造方法 |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5768641B2 (ja) * | 2010-10-08 | 2015-08-26 | Jfeスチール株式会社 | 耐食性および電気伝導性に優れたフェライト系ステンレス鋼およびその製造方法、ならびに固体高分子型燃料電池セパレータおよび固体高分子型燃料電池 |
JP6220393B2 (ja) | 2013-06-13 | 2017-10-25 | 東洋鋼鈑株式会社 | 金めっき被覆ステンレス材、および金めっき被覆ステンレス材の製造方法 |
EP3258523A4 (en) * | 2015-02-13 | 2018-01-31 | Nippon Steel & Sumitomo Metal Corporation | Separator for solid polymer fuel cell and method for producing same |
JP6414369B1 (ja) * | 2017-02-09 | 2018-10-31 | Jfeスチール株式会社 | 燃料電池のセパレータ用鋼板の基材ステンレス鋼板およびその製造方法 |
US11085120B2 (en) | 2017-04-25 | 2021-08-10 | Jfe Steel Corporation | Stainless steel sheet for fuel cell separators and production method therefor |
KR102391553B1 (ko) | 2017-10-25 | 2022-04-27 | 제이에프이 스틸 가부시키가이샤 | 연료 전지의 세퍼레이터용 스테인리스 강판의 제조 방법 |
CN113348273A (zh) | 2019-01-21 | 2021-09-03 | 杰富意钢铁株式会社 | 燃料电池的隔离件用的奥氏体系不锈钢板及其制造方法 |
CN111334699A (zh) * | 2019-12-18 | 2020-06-26 | 国家电投集团黄河上游水电开发有限责任公司 | 一种用于铝用炭素焙烧燃烧器合金材料 |
CA3168212A1 (en) * | 2020-03-12 | 2021-09-16 | Yoshitomo Fujimura | Ferritic stainless steel and method for manufacturing same |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010013684A (ja) * | 2008-07-02 | 2010-01-21 | Jfe Steel Corp | 接触電気抵抗の低い通電部品用ステンレス鋼およびその製造方法 |
JP2010514930A (ja) * | 2006-12-28 | 2010-05-06 | ポスコ | 高分子電解質膜燃料電池のバイポーラ板用ステンレス鋼の表面特性改善方法 |
WO2011089730A1 (ja) * | 2010-01-20 | 2011-07-28 | Jfeスチール株式会社 | 接触電気抵抗の低い通電部品用ステンレス鋼およびその製造方法 |
WO2012098689A1 (ja) * | 2011-01-17 | 2012-07-26 | Jfeスチール株式会社 | 燃料電池セパレータ用ステンレス鋼の製造方法、燃料電池セパレータ用ステンレス鋼、燃料電池セパレータ、ならびに燃料電池 |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR100240741B1 (ko) * | 1994-01-26 | 2000-01-15 | 에모또 간지 | 내부식성이 우수한 스테인레스강판의 제조방법 |
JP4629914B2 (ja) * | 2001-06-04 | 2011-02-09 | 日新製鋼株式会社 | 低温型燃料電池用セパレータ及びその製造方法 |
CN100552076C (zh) * | 2003-02-10 | 2009-10-21 | 杰富意钢铁株式会社 | 镀层附着性优良的合金化热镀锌钢板及其制造方法 |
JP2007026694A (ja) * | 2005-07-12 | 2007-02-01 | Nisshin Steel Co Ltd | 固体高分子型燃料電池用セパレータ及び固体高分子型燃料電池 |
JP2008091225A (ja) * | 2006-10-03 | 2008-04-17 | Nisshin Steel Co Ltd | 固体高分子型燃料電池用セパレータ及びその製造方法 |
KR100836480B1 (ko) * | 2006-12-28 | 2008-06-09 | 주식회사 포스코 | 연료전지 분리판인 스테인리스 강재의 표면처리방법 |
JP5309385B2 (ja) * | 2007-04-27 | 2013-10-09 | 日本金属株式会社 | ステンレス鋼製導電性部材およびその製造方法 |
TWI427159B (zh) * | 2007-04-27 | 2014-02-21 | 不鏽鋼製導電性構件及其製造方法 | |
US20130108945A1 (en) * | 2008-07-02 | 2013-05-02 | Jfe Steel Corporation | Stainless steel for conductive members with low contact electric resistance and method for producing the same |
KR100993412B1 (ko) * | 2008-12-29 | 2010-11-09 | 주식회사 포스코 | 고분자 연료전지 분리판용 스테인리스강 및 그 제조방법 |
US9130199B2 (en) * | 2009-07-23 | 2015-09-08 | Jfe Steel Corporation | Stainless steel for fuel cell having good corrosion resistance and method for producing the same |
JP5768641B2 (ja) * | 2010-10-08 | 2015-08-26 | Jfeスチール株式会社 | 耐食性および電気伝導性に優れたフェライト系ステンレス鋼およびその製造方法、ならびに固体高分子型燃料電池セパレータおよび固体高分子型燃料電池 |
-
2011
- 2011-07-29 JP JP2011166580A patent/JP5218612B2/ja active Active
-
2012
- 2012-07-25 US US14/131,030 patent/US20140154129A1/en not_active Abandoned
- 2012-07-25 WO PCT/JP2012/004736 patent/WO2013018320A1/ja active Application Filing
- 2012-07-25 EP EP12819761.3A patent/EP2738277A4/en not_active Withdrawn
- 2012-07-25 CN CN201280037588.7A patent/CN103717769B/zh active Active
- 2012-07-25 KR KR1020147003502A patent/KR20140039327A/ko active Search and Examination
- 2012-07-27 TW TW101127094A patent/TWI474539B/zh active
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2010514930A (ja) * | 2006-12-28 | 2010-05-06 | ポスコ | 高分子電解質膜燃料電池のバイポーラ板用ステンレス鋼の表面特性改善方法 |
JP2010013684A (ja) * | 2008-07-02 | 2010-01-21 | Jfe Steel Corp | 接触電気抵抗の低い通電部品用ステンレス鋼およびその製造方法 |
WO2011089730A1 (ja) * | 2010-01-20 | 2011-07-28 | Jfeスチール株式会社 | 接触電気抵抗の低い通電部品用ステンレス鋼およびその製造方法 |
WO2012098689A1 (ja) * | 2011-01-17 | 2012-07-26 | Jfeスチール株式会社 | 燃料電池セパレータ用ステンレス鋼の製造方法、燃料電池セパレータ用ステンレス鋼、燃料電池セパレータ、ならびに燃料電池 |
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Title |
---|
See also references of EP2738277A4 * |
Cited By (3)
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WO2021006099A1 (ja) * | 2019-07-09 | 2021-01-14 | Jfeスチール株式会社 | 硫化物系固体電池の集電体用のフェライト系ステンレス鋼板およびその製造方法 |
JP2021012839A (ja) * | 2019-07-09 | 2021-02-04 | Jfeスチール株式会社 | 硫化物系固体電池の集電体用のフェライト系ステンレス鋼板およびその製造方法 |
JP7057766B2 (ja) | 2019-07-09 | 2022-04-20 | Jfeスチール株式会社 | 硫化物系固体電池の集電体用のフェライト系ステンレス鋼板およびその製造方法 |
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EP2738277A4 (en) | 2015-08-19 |
US20140154129A1 (en) | 2014-06-05 |
TWI474539B (zh) | 2015-02-21 |
CN103717769B (zh) | 2016-04-27 |
EP2738277A1 (en) | 2014-06-04 |
KR20140039327A (ko) | 2014-04-01 |
CN103717769A (zh) | 2014-04-09 |
JP2013028849A (ja) | 2013-02-07 |
JP5218612B2 (ja) | 2013-06-26 |
TW201308724A (zh) | 2013-02-16 |
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