Patent Application
20240006623
The present invention relates to a surface-treated titanium material for a fuel cell separator and a method for manufacturing the same, and particularly relates to a surface-treated titanium material for a fuel cell separator capable of maintaining high conductivity for a long period of time, and a method for manufacturing the same.
A separator that partitions respective cells of a fuel cell has a role of forming a flow path of a fuel gas and causing a current generated from a cell to flow to an adjacent cell. Accordingly, a material for a fuel cell separator is required to have high conductivity and maintain the conductivity for a long period of time even in a corrosive atmosphere in the fuel cell.
As a separator material satisfying such requirements, for example, Patent Literature 1 discloses a separator material for a fuel cell in which a mixture layer in which titanium oxide mainly composed of rutile and carbon black are mixed is formed on a surface of a titanium substrate.
According to the separator material for a fuel cell disclosed in Patent Literature 1, since a mixture film contains carbon black that is stable against oxidation, it is possible to achieve both high conductivity and conductive corrosion resistance.
Patent Literature 1: JP2016-122642A
In order to increase power generation efficiency of the fuel cell, a width of a flow path groove of the fuel gas in the separator may be formed to be narrow.
However, when a separator having such narrow grooves is manufactured by press molding, the mixture layer containing titanium oxide mainly composed of rutile may be peeled off from the surface of the titanium substrate. In addition, since the above-mentioned mixture layer does not have sufficient toughness, numerous cracks are introduced into the mixture layer during the press molding, and a corrosive acidic solution in the fuel cell easily reaches the interface between the mixture layer and the titanium substrate through the cracks. As a result, there arises a problem that interfacial corrosion progresses and the conductivity decreases.
Therefore, it is desired to develop a separator material having a titanium substrate and a surface layer, which can improve adhesion between the surface layer and the substrate and toughness of the surface layer, and can maintain conductivity for a long period of time even when press molding for forming narrow grooves is performed.
The present invention has been made in view of the above problems, and an object of the present invention is to provide a surface-treated titanium material for a fuel cell separator, which has good toughness, and is excellent in adhesion between a surface layer and a substrate and capable of maintaining conductivity for a long period of time even when press molding is performed under severe conditions, and a method for manufacturing the surface-treated titanium material for a fuel cell separator.
The above-mentioned object of the present invention is achieved by the following configuration [1] according to the surface-treated titanium material for a fuel cell separator.
[1] A surface-treated titanium material for a fuel cell separator, including: a titanium substrate having a passive film on a surface thereof; and a surface layer formed on the titanium substrate, in which
The above-mentioned object of the present invention is achieved by the following configurations [2] or [3] according to a method for manufacturing a surface-treated titanium material for a fuel cell separator.
[2] A method for manufacturing the surface-treated titanium material for a fuel cell separator according to [1], including:
According to the present invention, it is possible to provide a surface-treated titanium material for a fuel cell separator, which has good toughness, and is excellent in adhesion between a surface layer and a substrate and capable of maintaining conductivity for a long period of time even when press molding is performed under severe conditions, and a method for manufacturing the surface-treated titanium material for a fuel cell separator.
Hereinafter, embodiments of the present invention (hereinafter, referred to as “the present embodiment”) will be described in detail. The present invention is not limited to the embodiments described below, and can be optionally modified and implemented without departing from the gist of the present invention.
In addition, in the present description, the word “to” indicating a numerical range is used to mean including numerical values described before and after the word as a lower limit value and an upper limit value.
In order to obtain a surface-treated titanium material that avoids interfacial peeling, has a titanium oxide layer with high toughness (cracks are less likely to occur), and can maintain high conductivity, the present inventors have conducted intensive studies. As a result, the inventors have found that it is effective to appropriately control a ratio of Ti2O3 to TiO2 in the titanium oxide layer and to reduce a region of voids. Hereinafter, the surface-treated titanium material for a fuel cell separator according to the present embodiment will be described in more detail. In the present description, the surface-treated titanium material for a fuel cell separator may be simply referred to as a surface-treated titanium material.
A surface-treated titanium material 1 includes a titanium substrate 2 having a passive film 3 on at least a part of a surface, and a surface layer 4 formed on the titanium substrate 2.
The surface layer 4 includes a titanium oxide layer 5 and carbon particles 6. Carbon particles 6a are dispersed in an inside of the titanium oxide layer 5, and some of carbon particles 6b adhere tightly to a surface of the titanium oxide layer 5. In addition, voids are inevitably formed at an interface F2 between the titanium substrate 2 and the surface layer 4.
On a surface of the titanium substrate 2, a passive film (amorphous titanium oxide layer) having a thickness of 3 nm to 10 nm originally exists, and the passive film 3 remains also in the surface-treated titanium material 1 obtained by a manufacturing method according to the present embodiment. A thickness of the remaining passive film 3 may be different from a thickness of the passive film originally exists on the surface of the titanium substrate 2, and the passive film 3 in the surface-treated titanium material 1 according to the present embodiment refers to a passive film remaining after the manufacture. Hereinafter, the passive film remaining after the manufacture is simply referred to as the passive film 3, and a portion of the titanium substrate 2 excluding the passive film 3 is referred to as a metallic titanium layer 2a.
The carbon particles 6 are stable against oxidation and serve as a conductive path through which a current generated from a cell flows to an adjacent cell.
Although depending on a size of the carbon particles 6, when a total film thickness T of the titanium oxide layer 5 and the passive film 3 is less than 25 nm, the carbon particles 6 cannot be sufficiently incorporated into the titanium oxide layer 5, and a desired conductivity cannot be obtained. Therefore, the total film thickness T of the titanium oxide layer 5 and the passive film 3 is 25 nm or more, and preferably 30 nm or more.
On the other hand, when the total film thickness T of the titanium oxide layer 5 and the passive film 3 is less than 50 nm, it is possible to prevent voids 7 from being excessively formed along the interface F2 between the titanium oxide layer 5 and the passive film 3 of the titanium substrate 2. As a result, when a fuel cell separator obtained by performing press molding on the surface-treated titanium material 1 is used, even when a corrosive acidic solution reaches the interface F2 through pores or cracks in the surface layer 4, the acidic solution can be prevented from spreading to the interface F2 because there are few voids 7 through which the acidic solution enters. As a result, corrosion can be avoided, and the conductivity of the fuel cell separator can be maintained. Therefore, the total film thickness T of the titanium oxide layer 5 and the passive film 3 is preferably less than 50 nm.
A thickness of the titanium oxide layer 5 varies depending on a plane orientation of crystal grains of the titanium substrate 2. A color of the titanium oxide layer 5 varies depending on the thickness thereof, and the color varies from yellow, orange, brown, purple, blue, and light blue in an ascending order of thickness. Therefore, when the surface is observed with an optical microscope or the like, each crystal grain has a different color, which indicates that the thickness of the titanium oxide layer 5 is not uniform. In the present description, the total film thickness T of the titanium oxide layer 5 and the passive film 3 refers to a total film thickness of the titanium oxide layer 5 and the passive film 3 in a case where a cross section of a portion with a color having the highest proportion is observed when viewed with an optical microscope. Hereinafter, the total film thickness T of the titanium oxide layer 5 and the passive film 3 may be simply referred to as a film thickness T.
First, a surface of the surface-treated titanium material 1 is observed with an optical microscope or the like, and a portion with a color having the highest proportion is subjected to cross-section processing using a Cross section polisher (CP (registered trademark)).
Next, a cross section is observed at a magnification of 300,000 times using the field emission scanning electron microscope (FE-SEM).
Thereafter, four regions where the carbon particles 6 do not exist on an outermost surface F3 of the titanium oxide layer 5 are searched in a range of an observation field of view, film thicknesses (distances from an interface F1 in the titanium substrate 2 between the metallic titanium layer 2a and the passive film 3 to the outermost surface F3 of the titanium oxide layer 5) T in the regions are measured, and an average of the four regions is set as the film thickness T.
In the present embodiment, a protective layer 10 is formed to protect the carbon particles 6 and the titanium oxide layer 5 before the cross-section processing using the CP is performed. The protective layer 10 can be obtained by, for example, forming an osmium film 8 on a surface of the surface layer 4 by vapor deposition and then forming a carbon film 9.
In
In the present embodiment, the titanium oxide layer 5 contains Ti2O3 and TiO2, and Ti2O3 has a metallic bonding component (High-temperature oxidation and high-temperature corrosion of metal material, 3rd edition, Table 2.3 on p40, edited by Japan Society of Corrosion Engineering). Therefore, it is considered that when an existing ratio of Ti2O3 in the titanium oxide layer 5 is increased, the titanium oxide layer 5 is easily plastically deformed and interfacial peeling is avoided when press molding is performed under severe conditions.
Accordingly, in the present embodiment, a content of Ti2O3 with respect to a content of TiO2 is calculated using a peak height indicating TiO2 of a rutile structure and a peak height indicating Ti2O3 when an analysis is performed by Raman spectroscopy.
In a case where peak separation is performed on a Raman spectrum of a combination of the surface layer and the passive film, a peak obtained in a range of 235 cm-1 to 252 cm−1 of a Raman shift represents TiO2, and a height of the peak is defined as I1 in the present embodiment. Similarly, a peak obtained in a range of 260 cm−1 to 276 cm−1 and a peak obtained in a range of 292 cm−1 to 303 cm−1 each represent Ti2O3, and heights of these peaks are defined as I2 and I3, respectively.
That is, the content of Ti2O3 with respect to the content of TiO2 is expressed by (I2+I3)/I1.
When (I2+I3)/I1 is less than 0.08, a content of TiO2 having high brittleness in the titanium oxide layer 5 is increased, and thus peeling of the titanium oxide layer 5 may occur when press molding is performed. In addition, even when peeling does not occur, many cracks are formed in the titanium oxide layer 5. As a result, the corrosive acidic solution generated in the fuel cell enters the interface F2 between the surface layer 4 and the titanium substrate 2 through a peeled interface or cracks to corrode the passive film 3 and/or titanium 2a adjacent to the passive film 3, so that the conductivity of the separator decreases.
Therefore, (I2+I3)/I1 is 0.08 or more, and preferably 0.2 or more.
Such titanium oxide including Ti2O3 mixed therein is not formed only by performing an oxidation treatment on a titanium substrate coated with carbon particles such as carbon black under a low-pressure oxygen atmosphere. It is obtained by, after the oxidation, performing a heat treatment (reduction treatment) in vacuum or in an inert gas atmosphere to cause oxygen of a titanium oxide (TiO2) having a rutile structure or an anatase structure formed in the oxidation treatment step to be diffused and absorbed into the titanium substrate. That is, since a part of oxygen of TiO2 is extracted by titanium, TiO2 is converted into Ti2O3.
However, since a volume of Ti2O3 per mole of titanium is about 16% smaller than that of rutile-type TiO2, a volume shrinkage of the titanium oxide layer 5 progresses as conversion from TiO2 to Ti2O3 progresses. Therefore, it is considered that the titanium oxide layer 5 may be made porous or an excessive tensile stress may be generated in the titanium oxide layer 5. Therefore, although Ti2O3 has a metallic bonding component, when the content of Ti2O3 is excessive, cracks are easily introduced into the titanium oxide layer 5 when the titanium oxide layer 5 is stretched by the press molding.
When the corrosive acidic solution generated in the fuel cell enters the inside of the titanium oxide layer 5 through the pores and cracks thus formed, the corrosive acidic solution reaches the interface F2 between the titanium substrate 2 and the surface layer 4 to corrode the passive film 3 and/or the metallic titanium layer 2a adjacent to the passive film 3. As a result, an amorphous titanium oxide layer having low conductivity is formed between the carbon particles 6 that impart conductivity and the titanium substrate 2, and the conductivity of the separator deteriorates. Therefore, it is also necessary to define an upper limit of the content of Ti2O3 in the titanium oxide layer 5.
When (I2+I3)/I1 exceeds 1.45, Ti2O3 is excessively formed in the titanium oxide layer 5, and thus the conductivity of the separator decreases. Therefore, (I2+I3)/I1 is 1.45 or less, and preferably 1.1 or less.
The reason why a sum (I2+I3) of the two peak heights is taken to represent the content of Ti2O3 is that, peak intensity is small with only one of the peaks, and it may be difficult to perform detection with only one of the peaks when the peak separation is performed by curve fitting of the Raman spectrum.
<L2/L1: 0.30 or less>
The voids 7 are inevitably formed at the interface F2 between the titanium substrate 2 and the surface layer 4. When there are many regions in which the voids 7 are formed, cracks or the like occur when the surface-treated titanium material 1 is subjected to the press molding, and a corrosive acidic solution enters an inside of the voids 7, and thus corrosion occurs in the interface F2, and the conductivity of the separator deteriorates.
In the present embodiment, an arbitrary cross section is observed at a magnification of, for example, 300,000 times using the FE-SEM, and a ratio of the regions in which the voids 7 are formed is appropriately defined. In a case where an arbitrary cross section is observed with the FE-SEM, a ratio of the regions in which the voids 7 are formed can be expressed by L2/L1 when a length of the interface F2 between the surface layer 4 and the titanium substrate 2 in the observation region is defined as L1 and a length of the voids 7 exist in the interface is defined as L2.
When L2/L1 exceeds 0.30, cracks are formed in the titanium oxide layer 5 when press molding is performed. Thereafter, when the obtained fuel cell separator is used, the corrosive acidic solution enters the voids 7 through the cracks, and the corrosive acidic solution spreads to the interface F2, thereby accelerating the corrosion of the passive film 3 and/or the metallic titanium layer 2a adjacent to the passive film 3.
Therefore, L2/L1 is preferably 0.30 or less. When no void 7 is observed in an arbitrary cross section observed with the FE-SEM, L2 is considered to be zero, and thus L2/L1 is zero.
A method for calculating a ratio of void regions will be described in detail with reference to
The void 7 has, for example, an elliptical shape extending in a horizontal direction, and an interface between the void 7 and the metallic titanium layer 2a has a contrast of a black linear shape (interface F2 between the passive film 3 and the titanium oxide layer 5). The interface is not a straight line and is undulated, but is assumed to be a straight line and a length of the void is measured based on an image.
In
As illustrated in
However, even when a value of (I2+I3)/I1 is within a range of the present invention, the contact resistance may exceed 15 mQ-cm2. This is because the contact resistance increases due to that the total film thickness T of the titanium oxide layer and the passive film is less than 25 nm, or that L2/L1 is 0.30 or more.
In the present embodiment, as the carbon particles 6, particles composed of carbon, or particles obtained by doping B, N, or the like into the particles composed of carbon can be used. Examples of the carbon particles 6 include carbon black, graphite, B-doped diamond particles, and N-doped diamond particles. The carbon particles may use one of the examples alone or a combination of two or more thereof. The carbon black is a carbon particle having a chain structure consisting of amorphous carbon. The carbon black is classified into furnace black, acetylene black, thermal black, or the like depending on the manufacturing method thereof, and any of those can be used. Examples of the graphite include artificial graphite and natural graphite.
An average particle diameter of the carbon particles 6 to be used is preferably 120 nm or less in terms of a median diameter (particle diameter at which a cumulative distribution reaches 50%: hereinafter, referred to as D50) based on a volume of aggregated carbon particles. When the average particle diameter of the carbon particles 6 is 120 nm or less, a ratio of small carbon particles 6 which are equal to or less than the thickness of the titanium oxide layer 5 increases, and thus an amount of the carbon particles incorporated into the titanium oxide layer increases. As a result, the number of conductive paths increases, and high conductivity can be obtained. The particle diameter (D50) of the carbon particles 6 is more preferably 70 nm or less.
By controlling the content of the carbon particles in the titanium oxide layer 5, a fuel cell separator having excellent conductivity can be obtained. When the content of the carbon particles in the titanium oxide layer 5 is 20% or more, excellent conductivity can be obtained. Therefore, the content of the carbon particles in the titanium oxide layer 5 is preferably 20% or more, and more preferably 25% or more.
(1), (2), and (3) of
In the present embodiment, the content of the carbon particles is calculated based on a backscattered electron image of a cross section of the surface layer, which is captured using an FE-SEM under conditions of an acceleration voltage of 2.0 keV and a magnification of 300,000 times. Specifically, the content can be obtained by determining a ratio of (Sc/(St+Sc)), when an area occupied by the carbon particles 6 incorporated into the inside of the titanium oxide layer 5 is defined as Sc and a total cross-sectional area of the titanium oxide layer 5 and the passive film 3 is defined as St.
The method for measuring the content of the carbon particles will be described in more detail with reference to (1), (2), and (3) of
First, as illustrated in (1) of
Next, as illustrated in (2) of
Thereafter, as illustrated in (3) of
Then, the number of black dots, which is a value proportional to Sc, and the number of dots in a region between the straight line A1 and the straight line A2, which is a value proportional to St+Sc, are measured, and Sc/(St+Sc) is calculated. Since the voids are also colored black at the time of binarization, the void portion is assumed to be a white dot to obtain the Sc.
A method for manufacturing a surface-treated titanium material for a fuel cell separator according to the present embodiment includes: a step of annealing a titanium substrate; a step of coating a surface of the annealed titanium substrate with carbon particles; an oxidation treatment step of thermally treating the titanium substrate coated with the carbon particles in an oxidizing atmosphere to form a titanium oxide layer including the carbon particles; a washing step of removing carbon particles not adhering tightly to the titanium oxide layer from a surface of the titanium oxide layer; and a reduction treatment step of heat-treating the titanium substrate having the titanium oxide layer formed thereon in vacuum or in an inert gas atmosphere to form a surface layer.
The manufacturing method will be described in detail below.
As the titanium substrate 2, a rolled titanium foil can be used.
An average carbon concentration from the outermost surface of the titanium substrate 2 to a position at a depth of 50 nm is preferably 10 atom % or less, and more preferably 7 atom % or less. As for carbon on the surface, titanium abrasion powder generated by rolling reacts with a lubricant to become Ti(C,O) having substantially the same composition of oxygen and carbon, and is embedded in a titanium surface. This Ti(C,O) is thermally decomposed in the following annealing step, and C is spread in titanium through solid solution diffusion, but when an amount of Ti(C,O) after the rolling is large, a large amount of Ti(C,O) that cannot be completely decomposed remains.
A titanium oxide layer is hardly formed on Ti(C,O) in an oxidation treatment step to be described later. In addition, Ti(C,O) itself has conductivity, but since Ti(C,O) easily corrodes in an acidic corrosive environment in the fuel cell to become titanium oxide, when a large amount of Ti(C, O) that cannot be completely decomposed remains, the contact resistance increases. The remaining Ti(C,O) that is not decomposed even after the annealing increases together with the average carbon concentration.
When the average carbon concentration from the outermost surface of the titanium substrate 2 to the position at a depth of 50 nm is 10 atom % or less, the amount of Ti(C,O) that cannot be completely decomposed is reduced, and an increase in contact resistance can be avoided. Therefore, the average carbon concentration is preferably 10 atom % or less, and more preferably 7 atom % or less.
A method for measuring the average carbon concentration from the outermost surface of the titanium substrate 2 to the position at a depth of 50 nm will be described below.
The carbon concentration from the outermost surface of the titanium substrate 2 to the position at a depth of 50 nm can be measured, for example, by performing composition analysis in a depth direction using an X-ray photoelectron spectroscopy (XPS). For example, in the XPS device, by causing Ar ions to collide against the surface of the titanium substrate at an acceleration voltage of 1 kV, the surface of the titanium substrate is etched in the depth direction at a depth in units of 0.5 nm to several nm, and the carbon concentration at the depth is measured. Thereafter, similarly, the operation of etching the surface of the titanium substrate at a depth in units of 0.5 nm to several nm and measuring the carbon concentration is repeated until an etching depth reaches 50 nm. By these operations, the carbon concentration at each depth from the surface is obtained. Then, measurement points are plotted when the horizontal axis represents an analysis depth and the vertical axis represents the carbon concentration, an area of a portion up to 50 nm surrounded by a polygonal line obtained by connecting respective points in order by a straight line and the horizontal axis is obtained, and the area is divided by 50 nm, thereby calculating the average carbon concentration up to 50 nm.
In general, carbon resulting from adsorption of an organic substance or the like existing in an atmosphere is detected from a surface layer of the titanium substrate 2. In the present description, in measurement of the carbon concentration, a portion excluding a surface layer portion (contaminated layer) of the titanium substrate 2 to which the organic substance or the like is adsorbed corresponds to the “outermost surface”. Therefore, the above-mentioned 50 nm indicates a value from the outermost surface as defined above to a depth of 50 nm. In addition, an analysis area is desirably an area of a circle having a diameter of 100 μm or more. The reason is that, since Ti(C,O) has a size of sub μm to several μm, when an average value of the carbon concentration on the surface of the titanium substrate is to be obtained, it is necessary to measure a region far larger than that of Ti(C,O).
The manufacturing method according to the present embodiment includes a step of annealing the titanium substrate. In the following step, the surface of the titanium substrate is variously changed, and for example, a coating layer obtained by applying carbon particles or a titanium oxide layer is formed, but in the following description, for convenience, the titanium substrate, including a layer formed on the surface, may be referred to as a titanium foil.
In order to enable press molding of narrow grooves, it is necessary to perform annealing on the titanium substrate 2 hardened by the rolling to soften the titanium substrate 2, that is, to reduce 0.2% yield strength of the titanium substrate 2. When the 0.2% yield strength of the titanium substrate 2 is high, spring back after the press molding becomes large, and the separator may warp or may not have a desired groove shape, which makes it difficult to assemble a fuel cell. Since the titanium substrate has anisotropy, the 0.2% yield strength differs between a longitudinal direction (referred to as an L direction) and a width direction (referred to as a T direction) of a coil. In order to enable the pressing of the narrow grooves, the 0.2% yield strength in the L direction is preferably 110 MPa to 150 MPa, and the 0.2% yield strength in the T direction is preferably 180 MPa to 215 MPa.
When the 0.2% yield strength is too low, the titanium foil may be broken by the press molding. Therefore, for example, a temperature of the rolled titanium foil is raised to 700° C. to 850° C., and the annealing is performed for about 20 seconds to 40 seconds. Although depending on a Fe concentration of titanium impurities that lowers a B phase precipitation temperature, by performing the annealing at 850° C. or lower, it is possible to avoid a B phase from precipitating at a grain boundary and to improve press moldability. That is, it is preferable to select a temperature and a time at which the B phase does not precipitate.
On the other hand, the annealing is possible even at 700° C. or lower, but when the temperature is low, a treatment time is preferably increased. In addition, when the carbon concentration of the surface of the rolled titanium foil is high, by increasing an annealing temperature and the treatment time, Ti(C,O) can be decomposed, C can diffuse into the titanium substrate, and an amount of the remaining Ti(C,O) can be reduced. In this way, annealing conditions can be appropriately changed in accordance with the carbon concentration of the surface within a range of annealing conditions in which the titanium foil is softened and the press molding is not affected.
The manufacturing method according to the present embodiment includes a step of coating the surface of the annealed titanium substrate 2 with carbon particles.
The carbon particles 6 can be applied on the titanium substrate 2 in a form of an aqueous or oleaginous dispersion liquid (also referred to as a dispersion coating material) in which the carbon particles 6 are dispersed. In addition, the carbon particles 6 may be directly applied onto the titanium substrate 2.
The dispersion coating material containing the carbon particles 6 may contain a binder resin and/or a surfactant. However, since the binder resin or the surfactant tend to decrease the conductivity, contents thereof are preferably as small as possible. In addition, the dispersion coating material may contain other additives as necessary.
As the binder resin, it is preferable to use a resin that is decomposed without residue by being heated in the oxidation treatment step. Examples of such a binder resin include an acrylic resin, a polyethylene resin, a polypropylene resin, a polystyrene resin, and a polyvinyl alcohol resin. Among these, the acrylic resin is preferable from a viewpoint that the lower a decomposition temperature, the less an effect on formation of the surface layer. The binder resin may use one of the examples alone or a combination of two or more thereof.
A blending ratio of the carbon particles 6 and the binder resin in the dispersion coating material is preferably 0.3 to 2.5 as (solid content of binder resin/solid content of carbon particles) in a solid content mass ratio. As the mass ratio decreases, the amount of the carbon particles 6 increases, and as a result, the conductivity is improved. Therefore, from a viewpoint of conductivity, the mass ratio is preferably 2.5 or less, and more preferably 2.3 or less. On the other hand, as the mass ratio increases, the amount of the binder resin increases. Therefore, when the mass ratio is large, adhesion between the titanium substrate 2 and a coating film is increased. Therefore, from a viewpoint of adhesion, the mass ratio is preferably 0.3 or more, and more preferably 0.4 or more.
As an aqueous medium, for example, water or ethanol can be used. As an oleaginous medium, for example, toluene or cyclohexanone can be used.
As described above, the average particle diameter of the carbon particles 6 is preferably 120 nm or less. Since the carbon particles 6 tend to easily form aggregates in a coating material, it is preferable to use a coating material designed not to form aggregates. For example, as the carbon particles 6, it is preferable to use carbon black in which dispersibility is enhanced by chemically bonding functional groups such as a carboxyl group to the surface to enhance repulsion between the particles.
An applying amount of only the carbon particles 6 on the surface of the titanium substrate 2, subtracting a binder resin component, is preferably 10 μg/cm2 or more, and more preferably 30 μg/cm2 or more from the viewpoint of conductivity. The applying amount of the carbon particles 6 is preferably 60 μg/cm2 or less. Even when the applying amount of the carbon particles 6 is larger than this, an effect of improving the conductivity tends to be saturated.
Examples of a method for applying the dispersion liquid in which the carbon particles 6 are dispersed to the titanium substrate 2 include, but are not limited to, a method using brush coating, a bar coater, a roll coater, a gravure coater, a die coater, a dip coater, or a spray coater. In addition, examples of a method for applying the carbon particles in a form of powder include a method in which a toner prepared using the carbon particles 6 is used, and the titanium substrate 2 is subjected to electrostatic coating with the toner.
The manufacturing method according to the present embodiment includes an oxidation treatment step of thermally treating the titanium substrate 2 coated with the carbon particles in an oxidizing atmosphere to form the titanium oxide layer 5 containing the carbon particles 6.
A tray 14 for holding a titanium foil 13 (titanium substrate 2 coated with carbon particles 6) is disposed in the sample chamber 11. In addition, in the heating chamber 12, two flat plate carbon heaters 16 of 20 cm×40 cm are disposed in parallel in a state of being separated by 7 cm.
The titanium foil 13 is placed on the tray 14 and mounted in the sample chamber 11 of the vacuum chamber 20 constituted as described above, and the vacuum chamber 20 is subjected to vacuum drawing. Next, the carbon heater 16 is heated to a predetermined temperature, oxygen is introduced into the vacuum chamber 20, and an inside of the vacuum chamber 20 is set to a predetermined pressure.
Thereafter, the tray 14 is conveyed from the sample chamber 11 to the heating chamber 12, heated for a predetermined time, and then returned to the sample chamber 11 to be allowed to cool. Thus, a titanium oxide layer 5 is formed.
An oxygen partial pressure during the oxidation treatment is preferably 10 Pa to 100 Pa. By setting the oxygen partial pressure to 10 Pa or more, a diffusion rate of titanium ions can be made appropriate when the titanium ions diffuse outward from the titanium substrate 2 to the titanium surface and are bonded to oxygen in the atmosphere to form the titanium oxide layer. As a result, it is possible to form a surface layer 4 having such a thickness that carbon particles serving as a conductive path are sufficiently incorporated therein.
In addition, by setting the oxygen partial pressure to 100 Pa or less, significant wear due to acceleration of combustion of the carbon particles can be avoided. Further, an increase in rate when oxygen diffuses inward into the titanium substrate 2 can be avoided, and formation of the titanium oxide layer 5 from an original surface of the titanium substrate 2 toward a titanium substrate 2 side can be prevented, so that good conductivity can be obtained.
When the carbon concentration of the surface of the titanium substrate 2 before the oxidation treatment is high, in order to improve corrosion resistance, a surface layer having a high carbon concentration may be dissolved and removed by pickling after annealing. In a case where such pickling is performed, a surface layer having a sufficient thickness is formed when an oxygen pressure is 1 Pa or more. The reason why a lower limit of the oxygen pressure at which a surface layer 4 having a sufficient thickness is formed, due to the outward diffusion of the titanium ions, varies is unclear, but it is considered that a difference in structure between the passive film on the surface of the titanium substrate 2 formed in the annealing step and the passive film formed after the pickling affects the diffusion rate in the passive film of the titanium ions that pass through the passive film from the titanium substrate 2 and are diffused outward to the surface.
As illustrated in
In order to form a desired titanium oxide layer 5, it is preferable to set a temperature rising rate and an attained temperature of the titanium foil 13, and a treatment time from carrying the titanium foil 13 into the heating chamber 12 to carrying the titanium foil 13 out therefrom. The temperature rising rate can be determined by a heater set temperature, the heater, and an emissivity of the titanium foil coated with the carbon particles, and the attained temperature can be determined by the heater set temperature and the treatment time.
When the applying amount of the carbon particles 6 onto the surface of the titanium substrate 2 is changed, the emissivity of the titanium foil 13 is changed, and the temperature rising rate is changed. In addition, when the type of the carbon particles 6 is changed, emissivity of the carbon particles 6 themselves is changed, and thus the temperature rising rate is changed. Further, when a material of the heater is changed, the emissivity of the heater, that is, a rate of heat release from the heater is changed, and thus the temperature rising rate is changed. As described above, since the temperature rising rate changes depending on various factors, although not determined uniquely, for example, in a case where the carbon heater is used, when the applying amount of the carbon particles 6 is 30 μg/cm2 or more and the carbon particles 6 are carbon black, it is preferable to set the treatment time to 7 seconds to 20 seconds and the attained temperature of the titanium substrate 2 to about 560° C. to 640° C.
The manufacturing method according to the present embodiment includes a washing step of removing carbon particles 6 not adhering tightly to the titanium oxide layer 5 from the surface of the titanium oxide layer 5.
In the coating layer obtained by coating the surface of the titanium substrate 2 with the carbon particles 6, only carbon particles 6 having a maximum particle diameter of about 100 nm are incorporated into the titanium oxide layer 5 from an interface between the titanium substrate 2 and the coating layer, or adhere tightly to the surface of the titanium oxide layer 5. Therefore, it is necessary to remove the carbon particles 6 not adhering tightly to the titanium oxide layer 5 from the surface of the titanium oxide layer 5. When the carbon particles 6 which does not adhere tightly to the titanium oxide layer 5 are not removed by washing, the carbon particles 6 may fall off due to press molding and adhere to a mold, and a pressing flaw may occur on the titanium foil 13 (titanium substrate 2 on which titanium oxide layer 5 is formed) to break the titanium foil 13. As the washing method, any method may be used as long as it is a method of removing excess carbon particles 6, such as a method of washing with water using a brush or a method of removing carbon particles by ultrasonic washing.
In the washing step, when at least the carbon particles 6 not adhering tightly to the surface of the titanium oxide layer 5 are removed, there is no adverse effect in the subsequent steps. Therefore, the carbon particles 6 adhering tightly to the surface of the titanium oxide layer 5 may be completely removed, or may partially remain adhering tightly to the surface.
The manufacturing method according to the present embodiment includes a reduction treatment step of heat-treating the titanium substrate 2 having the titanium oxide layer 5 formed thereon in vacuum or in an inert gas atmosphere to form the surface layer 4.
In the reduction treatment step, the vacuum chamber 20 used in the oxidation treatment step can be used.
First, the titanium foil 13 (titanium substrate 2 after washing) is placed on the tray 14, mounted in the sample chamber 11, and after vacuum drawing is performed, the carbon heater 16 is heated to a predetermined temperature. At the time of vacuum drawing, when oxygen supplying molecules such as H2O, O2, CO, and CO2 adsorbed on a wall surface of the vacuum chamber 20 are released, and a certain amount or more of the oxygen supplying molecules exist in the atmosphere in the vacuum chamber 20, the reduction treatment does not proceed. Therefore, a degree of vacuum in the vacuum chamber 20 is preferably less than 0.1 Pa, and more preferably 0.05 Pa or less.
The reduction treatment may be performed by introducing an inert gas such as Ar into the vacuum chamber 20, and increasing a pressure in the vacuum chamber 20 to 0.1 Pa or more. In this case, it is preferable to perform the vacuum drawing until the pressure becomes less than 0.1 Pa before introducing Ar into the vacuum chamber 20.
Thereafter, in the heating chamber 12, the titanium foil 13 is conveyed to between the two carbon heaters 16 heated to a predetermined temperature, heated for a predetermined time, and then returned to the sample chamber 11. Thus, the reduction treatment is performed and a desired surface layer 4 is formed.
As described above, by performing the reduction treatment step after the oxidation treatment step, the oxygen of the titanium oxide (TiO2) having a rutile structure or an anatase structure formed in the oxidation treatment step can be diffused and absorbed into the titanium substrate to generate Ti2O3. As a result, a titanium oxide layer 5 containing Ti2O3 and TiO2 at a desired ratio can be formed, and thus a surface layer 4 which is easily plastically deformed can be obtained.
As the conditions of the reduction treatment, it is preferable to appropriately set the temperature rising rate and the attained temperature of the titanium foil 13, and the treatment time from carrying the titanium foil 13 into the heating chamber 12 to carrying the titanium foil 13 out therefrom, in accordance with the conditions of the oxidation treatment, that is, an amount of titanium oxide formed by the oxidation treatment.
When the titanium oxide layer 5 is grown thick in the oxidation treatment step, unless an amount of oxygen in the titanium oxide layer 5 or the passive film 3 diffused into the metallic titanium layer 2a is increased by the reduction treatment, a formation amount of Ti2O3 is reduced, and adhesion between the surface layer 4 and the titanium substrate 2 and toughness cannot be obtained.
On the other hand, when the titanium oxide layer 5 is thin, unless the amount of oxygen in the titanium oxide layer 5 or the passive film 3 diffused into the metallic titanium layer 2a is reduced, Ti2O3 is excessively generated, and corrosion of the interface, that is, an increase in resistance is likely to occur.
When the temperature rising rate is low, that is, the emissivity of the heater is low, it takes time to increase the temperature of the titanium foil 13, and thus it is preferable to increase the treatment time.
On the other hand, when the temperature rising rate is fast, it is preferable to shorten the treatment time, but since the temperature rising time is kept substantially constant when the material of the heater is fixed, the attained temperature and the treatment time may be set as the conditions of the reduction treatment.
Further, even if the thickness of the titanium oxide layer is constant, when the reduction treatment is performed under a condition of a long reduction treatment time and/or under a condition of a high attained temperature, corrosion of the interface due to excessive reduction occurs, and the resistance of the fuel cell separator increases.
On the other hand, even if the thickness of the titanium oxide layer is constant, when the reduction treatment is performed under a condition of a short reduction treatment time and/or under a condition of a low attained temperature, the adhesion of the surface layer is insufficient or toughness is insufficient due to underreduction.
As described above, since the conditions of the reduction treatment vary depending on various factors, although not determined uniquely, in a case where strong oxidation (high temperature or long-time treatment) is performed, reduction is difficult to occur, and thus the conditions of the reduction treatment are preferred to be strengthened accordingly.
On the other hand, when weak oxidation is performed, reduction is likely to occur, and thus the conditions of the reduction treatment are preferred to be weakened.
For example, in the oxidation treatment step, when the attained temperature of the titanium foil 13 is set to a high temperature region of 620° C. to 635° C., the attained temperature of the titanium foil 13 in the reduction treatment step is preferably set to a temperature region of 525° C. to 610° C. In addition, in the oxidation treatment step, when the attained temperature of the titanium foil 13 is set to a low temperature region of 555° C. to less than 595° C., the attained temperature of the titanium foil 13 in the reduction treatment step is preferably set to a temperature region of 510° C. to 600° C. Further, in the oxidation treatment step, when the attained temperature of the titanium foil 13 is set to an intermediate temperature region of 595° C. to less than 620° C., the attained temperature of the titanium foil 13 in the reduction treatment step is preferably set to a temperature region of 515° C. to 610° C. With this setting, a desired resistance value can be obtained.
In addition, in both the oxidation treatment step and the reduction treatment step, other than the carbon heater 16, any heater can be used as long as the heater can heat the titanium foil 13 and is not oxidized and consumed in an oxidizing atmosphere, such as a sheath heater. However, since the emissivity varies depending on the material of the heater, it is preferable to optimize the treatment time.
In the manufacturing method according to the above-mentioned embodiment, manufacturing steps have been described in an order of the annealing step, the step of coating with carbon particles, the oxidation treatment step, the washing step, and the reduction treatment step, but the manufacturing steps may be performed in an order of the annealing step, the step of coating with carbon particles, the oxidation treatment step, the reduction treatment step, and the washing step, with the washing step being the last step.
That is, another method for manufacturing the surface-treated titanium material for a fuel cell separator according to the present embodiment includes: a step of annealing a titanium substrate; a step of coating a surface of the annealed titanium substrate with carbon particles; an oxidation treatment step of thermally treating the titanium substrate coated with the carbon particles in an oxidizing atmosphere to form a titanium oxide layer including the carbon particles; a reduction treatment step of heat-treating the titanium substrate having the titanium oxide layer formed thereon in vacuum or in an inert gas atmosphere to form a surface layer; and a washing step of removing carbon particles not adhering tightly to the titanium oxide layer from the surface of the titanium oxide layer.
However, in this case, in the reduction treatment step, since excess carbon particles 6 adhere to the surface of the titanium foil 13, the emissivity of the surface increases. As a result, when the reduction treatment is performed under the same heating conditions as those in the case where the reduction treatment is performed after the washing step, the temperature of the titanium foil 13 increases rapidly. Therefore, in the case where the washing step is performed after the reduction treatment step, a heater temperature in the reduction treatment step is preferably set to be lower.
Hereinafter, Examples and Comparative Examples of the surface-treated titanium material for a fuel cell separator manufactured by the manufacturing method according to the present embodiment will be described.
A surface-treated titanium material was manufactured by various manufacturing methods to be described below, and an effect of manufacturing conditions and the like on performance of the obtained surface-treated titanium material was investigated.
[Test 1. Effect of Ti2O3/TiO2 Ratio and Void Ratio on Performance]
Surface-treated titanium materials were manufactured by variously changing a Ti2O3/TiO2 ratio of ((I2+I3)/I1) and a void ratio of (L2/L1). Detailed manufacturing conditions, measurement conditions, and the like are as follows.
A titanium foil coil 26 having a width of 48 cm and rolled to a thickness of 0.1 mm was prepared, and a surface of a titanium foil 26a was subjected to composition analysis in the depth direction by an XPS. An average concentration of carbon at a depth of about 50 nm excluding the outermost surface of the titanium foil 26a was 3.9 atom %.
In the present Examples, a titanium substrate was annealed using a continuous annealing furnace 21 illustrated in
Using the continuous annealing furnace 21 implemented as described above, first, the titanium foil coil 26 was installed in the first chamber 22 and was subjected to vacuum drawing, and then the carbon heater 28 was heated to raise the heater temperature to 810° C. Next, Ar gas was introduced into the continuous annealing furnace 21 and a pressure in the furnace is set to about 2 Pa. Thereafter, a line speed was set such that a time for heating by the carbon heater 28 was 35 seconds, and the titanium foil 26a unwound from the titanium foil coil 26 was conveyed into the second chamber 23 and heated. Thereafter, the titanium foil 26a was conveyed to the third chamber 24, cooled in the furnace by radiation cooling or the like, wound inside the fourth chamber 25, and again formed into a titanium foil coil 27.
(Coating Step with Carbon Particles)
A titanium foil having a size of about 10 cm×20 cm was cut out from the annealed titanium foil coil 27, coated with a coating material containing carbon black on the surface of the titanium foil using a bar coater, and then dried using a dryer to form a coating film containing carbon black on the surface of the titanium foil. Similarly, a coating film was formed on a back surface. Carbon black having a particle diameter (D50) of 62 nm was used. In order to enhance the adhesion of the coating material, a coating material in which an acrylic resin was added in a weight ratio of 0.8 relative to the carbon black was used.
In addition, in order to measure an applying weight, a weight was measured for a titanium foil having the same size as that described above whose one surface was coated with the coating material and dried, and thereafter, the coating material was wiped off with a cloth containing ethanol, the weight was measured again, and a weight difference was calculated and divided by a coating area. The applying weight was about 60 μg/cm2. Therefore, the applying amount of the carbon black was calculated as 60÷1.8≈33 μg/cm2.
The oxidation treatment was performed using the vacuum chamber 20 illustrated in
By welding the thermocouple 15 to a center of the titanium foil 13 having the coating film containing carbon black formed on both surfaces thereof and heating the titanium foil 13 in the same manner as in the above-mentioned oxidation treatment step, a temperature change of the thermocouple when the titanium foil 13 is heated can be known. For example, as illustrated in
The titanium foil 13 was taken out from the vacuum chamber 20, the surface thereof was rubbed with a cloth impregnated with ethanol, and then the surface was rubbed with a sponge again while applying water thereto and dried, thereby washing and removing excess carbon black not adhering tightly to the surface of the titanium foil 13.
The reduction treatment was performed using the vacuum chamber 20 illustrated in
The titanium foil of which the treatment is finished (surface-treated titanium material) was cut such that a length of one side parallel to a rolling direction of the coil was 65 mm and a width of the other side perpendicular to the rolling direction was 20 mm. Then, on both sides apart from a center line in a length direction by 12.5 mm, reference lines were drawn in parallel with the center line with a marker pen, both ends in the length direction were held by a tensile tester to pull the titanium foil such that a length between the reference lines became 32.5 mm, and thus a press-molded simulated material was prepared under severe conditions with an elongation percentage of 30%.
Using such a contact resistance measuring instrument 30, the initial contact resistance (contact resistance before immersion) of each simulated material was measured.
In the test material 37, a resin sheet 35 having a thickness of 0.05 mm and having a hole with a diameter of 16 mm was stacked in the vicinity of a central portion of a press-molded simulated material 34 described above, and a carbon paper 36 having a width of about 20 mm was stacked on the resin sheet 35. The press-molded simulated material 34 and the carbon paper 36 were stacked so as to cover the hole of the resin sheet 35. Then, the three-layered test material 37 was inserted between the copper electrode 31a and the copper electrode 31b each having a diameter of 14 mm and a tip end area of 1.54 cm2, taking care to avoid the resin sheet be sandwiched between the electrodes. Thereafter, the load was set to 15.4 kg and the test material 37 was pressurized with the copper electrode 31a and the copper electrode 31b. Then, a resistance was measured by connecting one current terminal 32 of the four-terminal resistance measuring instrument 33 to the copper electrode 31a, connecting the other current terminal 32 to the copper electrode 31b, and at the same time, connecting one resistance measuring terminal 38a to the press-molded simulated material 34, and connecting the other resistance measuring terminal 38b to the carbon paper 36. Thereafter, the measured resistance value was multiplied by a contact area of 1.54 cm2 to calculate the initial contact resistance before immersion.
(Measurement of Contact Resistance after Immersion)
Contact resistance after the simulated material 34 was immersed in a corrosive acidic solution was measured, assuming that the fuel cell separator was used. As the corrosive acidic solution, an acidic solution obtained by adding NaF and NaCl to ion-exchanged water whose pH was adjusted to 3 by addition of sulfuric acid such that a fluorine ion concentration was 30 ppm and a chlorine ion concentration was 10 ppm was used.
First, the above-mentioned press-molded simulated material 34 was placed in a polyethylene container, immersed in the above-mentioned acidic solution, and covered with a lid, and the container was placed in a thermostatic bath at 80° C. and held for four days (96 hours). Thereafter, the container was taken out from the thermostatic bath, the titanium foil was taken out from the container, washed with ion-exchanged water and dried, and the contact resistance after immersion was measured by the same method as the method for measuring the initial contact resistance.
In the present Examples, those having a contact resistance of 15 mΩ·cm2 or less were considered acceptable.
(Measurement of Ti2O3/TiO2 Ratio)
Among resistance measurement portions of the titanium foil before the press-molded simulated material 34 was prepared, a region having an area of 1 cm2 was measured over a wave number range of 150 cm−1 to 2,000 cm−1 by Raman spectroscopic analysis. For the Raman spectroscopic analysis, a laser Raman microscope RAMANtouch (manufactured by Nanophoton Corporation) was used. In addition, measurement conditions were set as follows: laser wavelength: 532 nm; laser power: about 500 W/cm2; diffraction grating: 600 gr/mm; and slit width: 50 μm.
Next, a spectrum of 150 cm−1 to 800 cm−1 in which a peak derived from titanium oxide was observed was retrieved, and peak search and peak separation were performed.
The titanium oxide formed in the oxidation treatment step was almost only rutile, but by performing the reduction treatment, TiO2 in a form of rutile is reduced, and a small amount of TiO2 of an anatase structure and Ti2O3 were formed. As illustrated in
On the other hand, as illustrated in
Among surface-treated titanium materials obtained by variously changing the temperature during the oxidation treatment, the surface of a part of the surface-treated titanium materials was observed with an optical microscope, and a portion with a color having the highest surface ratio was subjected to cross-section processing with a Cross section polisher (CP). Then, a backscattered electron image of the cross section was captured by an FE-SEM (5-5000, manufactured by Hitachi High-Tech Corporation) at an acceleration voltage of 2.0 kV and a magnification of 300,000 times, and the ratio of a length occupied by voids to a length of the interface (void ratio: L2/L1) and the film thickness T were measured.
As illustrated in
In addition, the voids are also formed in the oxidation treatment step in which the titanium oxide layer is formed. In a mechanism in which titanium oxide is formed by the oxidation treatment, titanium atoms in the titanium substrate diffuse in the passive film on the surface of the titanium substrate, exit to the surface of the passive film, and react with oxygen in the furnace, thereby forming titanium oxide mainly having a rutile structure. Thereafter, the titanium atoms diffused from the titanium substrate diffuse in the passive film and the titanium oxide mainly composed of rutile formed on the surface thereof, reach the surface, and continue to react with oxygen in the furnace, whereby the titanium oxide layer grows. In this case, the titanium ions (in the titanium oxide layer, titanium takes a form of ions) diffused in the titanium oxide layer appear on the surface of the titanium oxide layer by exchanging a position with pores that exist in a titanium lattice in the titanium oxide layer. In addition, the pores diffuse into an interface between the titanium oxide and the passive film.
Some of the pores diffused in the interface diffuse in the passive film, but some are accumulated in the interface between the titanium oxide and the passive film and grow into voids. Therefore, when a temperature of the oxidation treatment is high or the time of the oxidation treatment is long, a diffusion amount of the pores increases, and thus an amount of pores accumulated in the interface between the titanium oxide and the passive film, that is, voids increase. That is, although there is some variation, formation of the voids is also substantially determined by only the conditions of the oxidation treatment.
Therefore, similarly to the film thickness, a formation amount of the voids can be considered to be substantially the same as long as the temperature and time of the oxidation treatment are the same, although there is some variation. Therefore, one or two test pieces were selected for each heater set temperature during oxidation, the void ratio of (L2/L1) and the film thickness T were measured, and all test pieces treated under the same oxidation conditions were regarded as having substantially the same void ratio and film thickness and measurements thereof were not performed.
Measurement results of temperatures at the time of oxidation treatment and reduction treatment, contact resistances at an initial stage and after immersion for four days, the Ti2O3/TiO2 ratio, the void ratio, and the film thickness T of each test piece are shown in Table 1 below. In Table 1, “-” indicates that measurement was not performed. In addition, in a column of the temperature of oxidation treatment, the estimated temperature of titanium foil was set to 15° C. higher than the heater set temperature for oxidation treatment. Further, in a column of the temperature of reduction treatment, the estimated temperature of titanium foil was set to 30° C. lower than the heater set temperature for reduction treatment.
As shown in Table 1, in each of Examples No. 1 to No. 12, since the Ti2O3/TiO2 ratio in Raman was within a range of 0.08 to 1.45 and the void ratio was all 0.3 or less, the contact resistance after immersion in a test solution for four days was 15 mΩ·cm2 or less. In this way, Examples No. 1 to No. 12 indicated that excellent conductivity can be maintained for a long period of time.
In contrast, the Ti2O3/TiO2 ratio was 1.66 in Comparative Example No. 1, which exceeded the upper limit of 1.45 of the range of the present invention, and thus the contact resistance after immersion in the test solution for four days exceeded 15 mΩ·cm2. The reason is considered to be that, formation of Ti2O3 was excessive due to a high temperature of reduction treatment compared to a low temperature of oxidation treatment.
The Ti2O3/TiO2 ratio was 0.00 in Comparative Example No. 2, which is less than the lower limit of 0.08 of the range of the present invention, and thus the contact resistance after immersion in the test solution for four days exceeded 15 mΩ·cm2. The reason is considered to be that, reduction was not effective and Ti2O3 was hardly formed due to a low temperature of reduction treatment compared to a high temperature of oxidation treatment, and thus at the time of preparation of the press-molded simulated material, partial peeling due to tension or formation of a large number of cracks occurred, and corrosion progressed.
In Comparative Example No. 3 and Comparative Example No. 4, the Ti2O3/TiO2 ratios were within the range of the present invention, but the void ratios were 0.326 and 0.348, respectively, which exceeded the upper limit of 0.3 of the range of the present invention, and thus the contact resistance after immersion in the test solution for four days exceeded 15 mΩ·cm2. The reason is considered to be that voids were excessively formed due to the high temperature of oxidation treatment.
Surface-treated titanium materials were manufactured by variously changing the particle diameter (D50) of the carbon particles and the conditions of the reduction treatment. Detailed manufacturing conditions, measurement conditions, and the like are as follows.
Annealing of a titanium foil coil having a width of 48 cm and a thickness of 0.1 mm was performed in the same manner as in Test 1.
(Coating Step with Carbon Particles)
A titanium foil unwound from the annealed titanium foil coil was installed on a die coating line, and both surfaces of the titanium foil were coated with the same coating material as that in Test 1 using a die coater such that an applying weight of the coating material after drying was 50 μg/cm2 to 70 μg/cm2 (28 μg/cm2 to 39 μg/cm2 in terms of carbon black). In the present Examples, two types of carbon black were used of which the particle diameters (D50) of the carbon particles (carbon black) were 62 nm and 109 nm.
The oxidation treatment was performed using the continuous annealing furnace 21 illustrated in
The oxidized titanium foil coil 27 was taken out from the continuous annealing furnace 21, and in order to remove excess carbon black not adhering tightly to the surface of the titanium foil 13, the titanium foil coil 27 was set in a continuous water washing equipment having a brush washing tank and an ultrasonic washing tank, and line washing was performed.
A titanium foil coil using carbon black having a particle diameter (D50) of 62 nm and a titanium foil coil using carbon black having a particle diameter (D50) of 109 nm were subjected to the reduction treatment using the continuous annealing furnace 21 illustrated in
A press-molded simulated material was prepared in the same manner as in Test 1.
(Measurement of Initial Contact Resistance and Contact Resistance after Immersion)
The initial contact resistance and the contact resistance after immersion for four days were measured for the press-molded simulated material in the same manner as in Test 1.
In the length direction of a surface between the standard lines of the press-molded simulated material pulled at an elongation percentage of 30%, a tape (Cellotape (registered trademark): product number 405 (manufactured by NICHIBAN CO., LTD.)) having a width of 12 mm and a length of about 5 cm was attached in a length of about 2 cm from one end portion of the tape in the length direction. Then, after the attached portion was rubbed with a soft cloth, the tape was pulled to such an extent that the tape was not peeled off such that the tape in a portion not adhered to an attached surface from the other end portion of the tape to a boundary of the attached portion of the tape was at 90° with respect to the attached surface. Thereafter, in a state where the angle of 90° was substantially maintained, a force was applied such that the tape was peeled off in about one second to two seconds, and the tape was peeled off from the press-molded simulated material. In this way, a tape peeling test was performed, and the adhesion of the surface layer was measured by visually observing the surface from which the tape was peeled off or the peeled tape.
(Measurement of Ti2O3/TiO2 Ratio)
Among resistance measurement portions of the titanium foil before the press-molded simulated material 34 was prepared, a region of 0.2 mm×0.2 mm was measured over a wave number range of 150 cm−1 to 2,000 cm−1 by Raman spectroscopic analysis, and the Ti2O3/TiO2 ratio was determined in the same manner as in Test 1. For the Raman spectroscopic analysis, a microscopic laser Raman spectrometer LabRAM HR-800 (manufactured by Jobin Yvon) was used. In addition, measurement conditions were set as follows: laser wavelength: 514.6 nm; laser power: 20 mW; diffraction grating: 300 gr/mm; confocal hole diameter: 100 μm; and exposure time×the number of times of integration: 120 seconds×8 times.
The surface-treated titanium foil was cut into a piece having a size of 2 cm×5 cm, a weight thereof was measured, then a surface layer on one surface was polished and removed by buffing, and carbon black was burned by a burning method. For the burning, a carbon/sulfur analyzer CS844 (manufactured by LECO JAPAN CORPORATION) was used.
Then, an amount of CO2 generated by the burning was quantified to calculate the weight of carbon black incorporated into the surface layer on the one surface. In addition, a surface area of the one surface was determined by dividing the weight of the titanium foil measured in advance by a thickness (0.1 mm) of the titanium foil and the density of titanium, and the weight of the carbon black in the surface layer per unit area was determined by dividing the calculated weight of the carbon black by the surface area of the one surface.
Measurement results of a particle diameter (D50) of the carbon particles, estimated temperatures of the titanium foil at the time of oxidation treatment and reduction treatment, contact resistances at an initial stage and after immersion for four days, the Ti2O3/TiO2 ratio, and the weight of carbon black of each test piece are shown in Table 2 below. Based on
In Example No. 13 and Example No. 14, the Ti2O3/TiO2 ratio was within the range of 0.08 to 1.45, and thus the contact resistance after immersion in the test solution for four days was 15 mΩ·cm2 or less. In addition, a result was shown that in the tape peeling test, peeling was not visually observed, and the adhesion was also good. When Example No. 13 and Example No. 14 are compared, although the Ti2O3/TiO2 ratios were almost the same, the contact resistance in Example No. 13 in which the particle diameter D50 is 62 nm is lower. The reason is considered to be that, the weight of carbon black per cm2 in the surface layer, that is, a proportion of the carbon black in the surface layer incorporated into the surface layer is larger in Example No. 13 in which the particle diameter D50 is small than in Example No. 14 in which the particle diameter D50 is large, and thus the number of conductive paths is increased. As described above, the smaller the particle diameter D50 of the carbon particles, the larger the conductivity.
On the other hand, in Comparative Example No. 6, since the surface layer does not contain carbon particles, the initial contact resistance shows a good value, but the contact resistance after immersion for four days significantly exceeded 15 mΩ·cm2. From this result, it was shown that the carbon particles (carbon black) were a stable conductive path, and the long-term stability of conductivity was not maintained unless carbon black was contained.
Surface-treated titanium materials were manufactured by variously changing the film thickness T. In Test 3, in order to confirm the effect of the film thickness T, three types of heater set temperatures of 615° C., 595° C., and 535° C. at the time of oxidation treatment were set to prepare test pieces. Manufacturing conditions and measurement conditions of the test pieces are shown below.
A surface-treated titanium material was manufactured in the same manner as in Test 1.
(Measurement of Initial Contact Resistance and Contact Resistance after Immersion)
The initial contact resistance and the contact resistance after immersion for four days were measured for the press-molded simulated material in the same manner as in Test 1.
(Measurement of Ti2O3/TiO2 Ratio) The Ti2O3/TiO2 Ratio was measured in the same manner as in Test 1.
The surface of the surface-treated titanium material obtained by variously changing the temperature during the oxidation treatment was observed with an optical microscope, and a portion with a color having the highest surface ratio was subjected to cross-section processing with a Cross section polisher (CP). Then, a backscattered electron image of the cross section was captured by an FE-SEM (S-5000, manufactured by Hitachi High-Tech Corporation) at an acceleration voltage of 2.0 kV and a magnification of 300,000 times, and the film thickness T was measured. In addition, the ratio of a length occupied by voids to a length of the interface (void ratio: L2/L1) was also measured.
The portion with a color having the highest surface ratio of the surface-treated titanium material was subjected to cross-section processing using a CP, the cross section thereof was captured by the FE-SEM, and the image was binarized in a region from a position where the interface between the passive film and the metallic titanium layer was as straight as possible to a position above the interface by the film thickness T. In this case, the carbon black was set to black, the titanium oxide layer was set to white, and a portion protruding from the surface of the titanium oxide layer was not included as the carbon black. An area occupied by the carbon black was defined as Sc, and a total cross-sectional area of the titanium oxide layer and the passive film was defined as St.
Then, the number of black dots, which is a value proportional to Sc, and the number of black and white dots, which is a value proportional to St+Sc, were measured, and a content (%) was calculated as {Sc/(St+Sc)}×100.
Measurement results of temperatures at the time of oxidation treatment and reduction treatment, contact resistances at the initial stage and after immersion for four days, the Ti2O3/TiO2 ratio, the void ratio, the film thickness T, and the content of carbon black of each test piece are shown in Table 3 below.
[Table 3]
As shown in Table 3, in Example No. 15 and Example No. 16, the film thickness T exceeded 25 nm, the Ti2O3/TiO2 ratio was within the range of 0.08 to 1.45, and the void ratio was also within the range of the present invention, and thus the contact resistance after immersion in a test solution for four days was 15 mΩ·cm2 or less.
On the other hand, in Comparative Example No. 7, the Ti2O3/TiO2 ratio and the void ratio were within the range of the present invention, but the film thickness was 21 nm, which was less than the lower limit of the range of the present invention, and thus the contact resistance after immersion in the test solution for four days exceeded 15 mΩ·cm2.
On the other hand, in each of Example No. 15 and Example No. 16, the carbon particles 6 were incorporated into the titanium oxide layer 5 and dispersed.
(1), (2), and (3) of
An effect of presence or absence of annealing to the titanium substrate on the 0.2% yield strength of the obtained surface-treated titanium material was confirmed.
The continuous annealing furnace 21 illustrated in
On the other hand, the titanium rolled foil that was not annealed was subjected to the surface treatment in the same manner as in Test 1, and 0.2% yield strength in the longitudinal direction (L direction) and the width direction (T direction) of the coil were measured. Six coils were annealed and four coils were not annealed, and the 0.2% yield strengths thereof were measured.
Measurement results of the 0.2% yield strength in the L direction and the T direction are shown in Table 4 below.
As shown in Table 4, in Example No. 17 to Example No. 22, surface-treated titanium materials were prepared using the annealed titanium substrate, the 0.2% yield strength in the L direction was 119 MPa to 143 MPa, and the 0.2% yield strength in the T direction was 185 MPa to 208 MPa.
A range of the 0.2% yield strength was preferably 110 MPa to 150 MPa in the L direction and 180 MPa to 215 MPa in the T direction. Therefore, the surface-treated titanium materials of Examples were all within the preferable range of the 0.2% yield strength, although there is some variation.
On the other hand, in Comparative Example No. 8 to Comparative Example No. 11, surface-treated titanium materials were prepared using the titanium substrate which was not annealed, the 0.2% yield strength in the L direction was 207 MPa to 239 MPa, and the 0.2% yield strength in the T direction was 230 MPa to 257 MPa, which were higher than the preferable range. From these results, it was shown that a step of annealing the titanium substrate is necessary, and when this step is not performed, the 0.2% yield strength becomes too high and a desired shape cannot be obtained when press molding of narrow grooves was performed.
Although various embodiments have been described above with reference to the drawings, it is needless to say that the present invention is not limited to such examples. It will be apparent to those skilled in the art that various alterations, modifications can be conceived within the scope of the claims, and it should be understood that they also justifiably belong to the technical scope of the present invention. Each component in the embodiments described above may be combined arbitrarily in the range without deviating from the spirit of the invention.
The present application is based on a Japanese Patent Application (Patent Application No. 2020-197464) filed on Nov. 27, 2020, the contents of which are incorporated herein by reference.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2020-197464 | Nov 2020 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2021/042691 | 11/19/2021 | WO |
