It is desirable to produce a ferritic stainless steel with corrosion resistance comparable to that of ASTM Type 304 stainless steel but that is substantially nickel-free, dual stabilized with titanium and columbium to provide protection from intergranular corrosion, and contains chromium, copper, and molybdenum to provide pitting resistance without sacrificing stress corrosion cracking resistance. Such a steel is particularly useful for commodity steel sheet commonly found in commercial kitchen applications, architectural components, and automotive applications, including but not limited to commercial and passenger vehicle exhaust and selective catalytic reduction (SCR) components.
In the ferritic stainless steels, the inter-relationship of and amount of titanium, columbium, carbon, and nitrogen are controlled to achieve subequilibrium surface quality, substantially equiaxed cast grain structure, and substantially full stabilization against intergranular corrosion. In addition, the inter-relationship of chromium, copper, and molybdenum is controlled to optimize corrosion resistance.
Subequilibrium melts are typically defined as compositions with titanium and nitrogen levels low enough so that they do not form titanium nitrides in the alloy melt. Such precipitates can form defects, such as surface stringer defects or laminations, during hot or cold rolling. Such defects can diminish formability, corrosion resistance, and appearance.
Timax=0.0044(N−1.027) Equation 1:
where Timax is the maximum concentration of titanium by percent weight, and N is the concentration of nitrogen by percent weight. All concentrations herein will be reported by percent weight, unless expressly noted otherwise.
Using Equation 1, if the nitrogen level is maintained at or below 0.020% in an embodiment, then the titanium concentration for that embodiment should be maintained at or below 0.25%. Allowing the titanium concentration to exceed 0.25% can lead to the formation of titanium nitride precipitates in the molten alloy. However,
Embodiments of the ferritic stainless steels exhibit an equiaxed cast and rolled and annealed grain structure with no large columnar grains in the slabs or banded grains in the rolled sheet. This refined grain structure can improve formability and toughness. To achieve this grain structure, there should be sufficient titanium, nitrogen and oxygen levels to seed the solidifying slabs and provide sites for equiaxed grains to initiate. In such embodiments, the minimum titanium and nitrogen levels are shown in
Timin=0.0025/N Equation 2:
where Timin is the minimum concentration of titanium by percent weight, and N is the concentration of nitrogen by percent weight.
Using the Equation 2, if the nitrogen level is maintained at or below 0.02% in an embodiment, the minimum titanium concentration is 0.125%. The parabolic curve depicted in
Fully stabilized melts of the ferritic stainless steels must have sufficient titanium and columbium to combine with the soluble carbon and nitrogen present in the steel. This helps to prevent chromium carbide and nitrides from forming and lowering the intergranular corrosion resistance. The minimum titanium and carbon necessary to lead to full stabilization is best represented by the following equation:
Ti+Cbmin=0.2%+4(C+N) Equation 3:
where Ti is the amount of titanium by percent weight, Cbmin is the minimum amount of columbium by percent weight, C is the amount of carbon by percent weight, and N is the amount of nitrogen by percent weight.
In the embodiments described above, the titanium level necessary for an equiaxed grain structure and subequilibrium conditions was determined when the maximum nitrogen level was 0.02%. As explained above, the respective Equations 1 and 2 yielded 0.125% minimum titanium and 0.25% maximum titanium. In such embodiments, using a maximum of 0.025% carbon and applying Equation 3, would require minimum columbium contents of 0.25% and 0.13%, respectively for the minimum and maximum titanium levels. In some such embodiments, the aim for the concentration of columbium would be 0.25%.
In certain embodiments, keeping the copper level between 0.40-0.80% in a matrix consisting of about 21% Cr and 0.25% Mo one can achieve an overall corrosion resistance that is comparable if not improved to that found in commercially available Type 304L. The one exception may be in the presence of a strongly acidic reducing chloride like hydrochloric acid. The copper-added alloys show improved performance in sulfuric acid. When the copper level is maintained between 0.4-0.8%, the anodic dissolution rate is reduced and the electrochemical breakdown potential is maximized in neutral chloride environments. In some embodiments, the optimal Cr, Mo, and Cu level, in weight percent satisfies the following two equations:
20.5≦Cr+3.3Mo Equation 4:
0.6≦Cu+Mo≦1.4 when Cumax<0.80 Equation 5:
Embodiments of the ferritic stainless steel can contain carbon in amounts of about 0.020 or less percent by weight.
Embodiments of the ferritic stainless steel can contain manganese in amounts of about 0.40 or less percent by weight.
Embodiments of the ferritic stainless steel can contain phosphorus in amounts of about 0.030 or less percent by weight.
Embodiments of the ferritic stainless steel can contain sulfur in amounts of about 0.010 or less percent by weight.
Embodiments of the ferritic stainless steel can contain silicon in amounts of about 0.30-0.50 percent by weight. Some embodiments can contain about 0.40% silicon.
Embodiments of the ferritic stainless steel can contain chromium in amounts of about 20.0-23.0 percent by weight. Some embodiments can contain about 21.5-22 percent by weight chromium, and some embodiments can contain about 21.75% chromium.
Embodiments of the ferritic stainless steel can contain nickel in amounts of about 0.40 or less percent by weight.
Embodiments of the ferritic stainless steel can contain nitrogen in amounts of about 0.020 or less percent by weight.
Embodiments of the ferritic stainless steel can contain copper in amounts of about 0.40-0.80 percent by weight. Some embodiments can contain about 0.45-0.75 percent by weight copper and some embodiments can contain about 0.60% copper.
Embodiments of the ferritic stainless steel can contain molybdenum in amounts of about 0.20-0.60 percent by weight. Some embodiments can contain about 0.30-0.5 percent by weight molybdenum, and some embodiments can contain about 0.40% molybdenum.
Embodiments of the ferritic stainless steel can contain titanium in amounts of about 0.10-0.25 percent by weight. Some embodiments can contain about 0.17-0.25 percent by weight titanium, and some embodiments can contain about 0.21% titanium.
Embodiments of the ferritic stainless steel can contain columbium in amounts of about 0.20-0.30 percent by weight. Some embodiments can contain about 0.25% columbium.
Embodiments of the ferritic stainless steel can contain aluminum in amounts of about 0.010 or less percent by weight.
The ferritic stainless steels are produced using process conditions known in the art for use in manufacturing ferritic stainless steels, such as the processes described in U.S. Pat. Nos. 6,855,213 and 5,868,875.
In some embodiments, the ferritic stainless steels may also include other elements known in the art of steelmaking that can be made either as deliberate additions or present as residual elements, i.e., impurities from steelmaking process.
A ferrous melt for the ferritic stainless steel is provided in a melting furnace such as an electric arc furnace. This ferrous melt may be formed in the melting furnace from solid iron bearing scrap, carbon steel scrap, stainless steel scrap, solid iron containing materials including iron oxides, iron carbide, direct reduced iron, hot briquetted iron, or the melt may be produced upstream of the melting furnace in a blast furnace or any other iron smelting unit capable of providing a ferrous melt. The ferrous melt then will be refined in the melting furnace or transferred to a refining vessel such as an argon-oxygen-decarburization vessel or a vacuum-oxygen-decarburization vessel, followed by a trim station such as a ladle metallurgy furnace or a wire feed station.
In some embodiments, the steel is cast from a melt containing sufficient titanium and nitrogen but a controlled amount of aluminum for forming small titanium oxide inclusions to provide the necessary nuclei for forming the as-cast equiaxed grain structure so that an annealed sheet produced from this steel also has enhanced ridging characteristics.
In some embodiments, titanium is added to the melt for deoxidation prior to casting. Deoxidation of the melt with titanium forms small titanium oxide inclusions that provide the nuclei that result in an as-cast equiaxed fine grain structure. To minimize formation of alumina inclusions, i.e., aluminum oxide, Al2O3, aluminum may not be added to this refined melt as a deoxidant. In some embodiments, titanium and nitrogen can be present in the melt prior to casting so that the ratio of the product of titanium and nitrogen divided by residual aluminum is at least about 0.14.
If the steel is to be stabilized, sufficient amount of the titanium beyond that required for deoxidation can be added for combining with carbon and nitrogen in the melt but preferably less than that required for saturation with nitrogen, i.e., in a sub-equilibrium amount, thereby avoiding or at least minimizing precipitation of large titanium nitride inclusions before solidification.
The cast steel is hot processed into a sheet. For this disclosure, the term “sheet” is meant to include continuous strip or cut lengths formed from continuous strip and the term “hot processed” means the as-cast steel will be reheated, if necessary, and then reduced to a predetermined thickness such as by hot rolling. If hot rolled, a steel slab is reheated to 2000° to 2350° F. (1093°-1288° C.), hot rolled using a finishing temperature of 1500-1800° F. (816-982° C.) and coiled at a temperature of 1000-1400° F. (538-760° C.). The hot rolled sheet is also known as the “hot band.” In some embodiments, the hot band may be annealed at a peak metal temperature of 1700-2100° F. (926-1149° C.). In some embodiments, the hot band may be descaled and cold reduced at least 40% to a desired final sheet thickness. In other embodiments, the hot band may be descaled and cold reduced at least 50% to a desired final sheet thickness. Thereafter, the cold reduced sheet can be final annealed at a peak metal temperature of 1700-2100° F. (927-1149° C.).
The ferritic stainless steel can be produced from a hot processed sheet made by a number of methods. The sheet can be produced from slabs formed from ingots or continuous cast slabs of 50-200 mm thickness which are reheated to 2000° to 2350° F. (1093°-1288° C.) followed by hot rolling to provide a starting hot processed sheet of 1-7 mm thickness or the sheet can be hot processed from strip continuously cast into thicknesses of 2-26 mm. The present process is applicable to sheet produced by methods wherein continuous cast slabs or slabs produced from ingots are fed directly to a hot rolling mill with or without significant reheating, or ingots hot reduced into slabs of sufficient temperature to be hot rolled in to sheet with or without further reheating.
To prepare ferritic stainless steel compositions that resulted in an overall corrosion resistance comparable to Type 304L austenitic stainless steel a series of laboratory heats were melted and analyzed for resistance to localized corrosion.
The first set of heats was laboratory melted using air melt capabilities. The goal of this series of air melts was to better understand the role of chromium, molybdenum, and copper in a ferritic matrix and how the variations in composition compare to the corrosion behavior of Type 304L steel. For this study the compositions of embodiments used in the air melts investigated are set forth in Table 1 as follows:
Both ferric chloride immersion and electrochemical evaluations were performed on all the above mentioned chemistries in Table 1 and compared to the performance of Type 304L steel.
Following methods described in ASTM 648 Ferric Chloride Pitting Test Method A, specimens were evaluated for mass loss after a 24 hour exposure to 6% Ferric Chloride solution at 50° C. This test exposure evaluates the basic resistance to pitting corrosion while exposed to an acidic, strongly oxidizing, chloride environment.
The screening test suggested that higher chromium bearing ferritic alloys that have a small copper addition would result in the most corrosion resistance composition within the series. The composition having the highest copper content of 1% did not perform as well as the other chemistries. However, this behavior may have been as a result of less than ideal surface quality due to the melting process.
A closer investigation of the passive film strength and repassivation behavior was studied using electrochemical techniques that included both corrosion behavior diagrams (CBD) and cycle polarization in a deaerated, dilute, neutral chloride environment. The electrochemical behavior observed on this set of air melts showed that a combination of approximately 21% Cr while in the presence of approximately 0.5% Cu and a small Mo addition achieved three primary improvements to Type 304L steel. First, the copper addition appeared to slow the initial anodic dissolution rate at the surface; second, the copper and small molybdenum presence in the 21% Cr chemistry assisted in a strong passive film formation; and third, the molybdenum and high chromium content assisted in the improved repassivation behavior. The level of copper in the 21Cr+ residual Mo melt chemistry did appear to have an “optimal” level in that adding 1% Cu resulted in diminished return. This confirms the behavior observed in the ferric chloride pitting test. Additional melt chemistries were submitted for vacuum melting in hopes to create cleaner steel specimens and determine the optimal copper addition in order to achieve the best overall corrosion resistance.
The second set of melt chemistries set forth in Table 2 was submitted for vacuum melt process. The compositions in this study are shown below:
The above mentioned heats varied mainly in copper content. Additional vacuum heats, of the compositions set forth in Table 3, were also melted for comparison purposes. The Type 304L steel used for comparison was commercially available sheet.
The chemistries of Table 3 were vacuum melted into ingots, hot rolled at 2250 F (1232° C.), descaled and cold reduced 60%. The cold reduced material had a final anneal at 1825 F (996° C.) followed by a final descale.
Comparison studies performed on the above mentioned vacuum melts of Example 2 (identified by their ID numbers) were chemical immersion tested in hydrochloric acid, sulfuric acid, sodium hypochlorite, and acetic acid.
1% Hydrochloric Acid.
As shown in
5% Sulfuric Acid.
As shown in
Acetic Acid and Sodium Hypochlorite.
In acid immersions consisting of acetic acid and 5% sodium hypochlorite, the corrosion behavior was comparable to that of Type 304L steel. The corrosion rates were very low and no true trend in copper addition was observed in the corrosion behavior. All investigated chemistries of Example 2 having a chromium level above 20% were within 1 mm/yr of Type 304L steel.
Electrochemical evaluations including corrosion behavior diagrams (CBD) and cyclic polarization studies were performed and compared to the behavior of Type 304L steel.
Corrosion behavior diagrams were collected on the vacuum heat chemistries of Example 2 and commercially available Type 304L in 3.5% sodium chloride in order to investigate the effects of copper on the anodic dissolution behavior. The anodic nose represents the electrochemical dissolution that takes place at the surface of the material prior to reaching a passive state. As shown in
Cyclic polarization scans were collected on the experimental chemistries of Examples 2 and commercially available Type 304L steel in 3.5% sodium chloride solution. These polarization scans show the anodic behavior of the ferritic stainless steel through active anodic dissolution, a region of passivity, a region of transpassive behavior and the breakdown of passivity. Additionally the reverse of these polarization scans identifies the repassivation potential.
The breakdown potential exhibited in the above mentioned cyclic polarization scans was documented as shown in
Much like the anodic dissolution rate, the addition of copper, as shown by the graph of the line identified as Fe21CrXCu0.25Mo in
When evaluating the repassivation behavior of the vacuum melted chemistries of Example 2 it showed that a chromium level of 21% and a small molybdenum addition can maximize the repassivation reaction. The relationship of copper to the repassivation potential appeared to become detrimental as the copper level increased, as shown by the graph of the line identified as Fe21CrXCu0.25Mo in
A ferritic stainless steel of the composition set forth below in Table 4 (ID 92, Example 2) was compared to Type 304L steel with the composition set forth in Table 4:
The two materials exhibited the following mechanical properties set forth in Table 5 when tested according to ASTM standard tests:
The material of Example 2, ID 92 exhibits more electrochemical resistance, higher breakdown potential, and higher repassivation potential than the comparative Type 304L steel, as shown in
It will be understood various modifications may be made to this invention without departing from the spirit and scope of it. Therefore, the limits of this invention should be determined from the appended claims.
This application is a non-provisional patent application claiming priority from provisional application Ser. No. 61/619,048 entitled “21% Cr Ferritic Stainless Steel,” filed on Apr. 2, 2012. The disclosure of application Ser. No. 61/619,048 is incorporated herein by reference.
Number | Name | Date | Kind |
---|---|---|---|
2447897 | Clarke, Jr. | Aug 1948 | A |
2797993 | Tanczyn | Jul 1957 | A |
3833359 | Murakami et al. | Sep 1974 | A |
4154602 | Kaito et al. | May 1979 | A |
4690798 | Narutani et al. | Sep 1987 | A |
5217544 | Baltenneck et al. | Jun 1993 | A |
5230752 | Bourgain et al. | Jul 1993 | A |
5304259 | Miyakusu et al. | Apr 1994 | A |
5395583 | Potgieter et al. | Mar 1995 | A |
5427635 | Bletton et al. | Jun 1995 | A |
5492575 | Teraoka et al. | Feb 1996 | A |
5565167 | Fujimoto et al. | Oct 1996 | A |
5656237 | Terrien et al. | Aug 1997 | A |
5714115 | Speidel et al. | Feb 1998 | A |
5773734 | Young | Jun 1998 | A |
5779820 | Hauser et al. | Jul 1998 | A |
5785924 | Beguinot et al. | Jul 1998 | A |
5795411 | Terrien et al. | Aug 1998 | A |
5830408 | Azuma et al. | Nov 1998 | A |
5868875 | Yoshitake et al. | Feb 1999 | A |
6033625 | Nagashima et al. | Mar 2000 | A |
6048416 | Hauser et al. | Apr 2000 | A |
6056917 | Chesseret et al. | May 2000 | A |
6086689 | Sassoulas et al. | Jul 2000 | A |
6096441 | Hauser et al. | Aug 2000 | A |
6106639 | Marandel et al. | Aug 2000 | A |
6110300 | Brada et al. | Aug 2000 | A |
6123784 | Havette | Sep 2000 | A |
6159310 | Inoue et al. | Dec 2000 | A |
6168756 | Hirasawa et al. | Jan 2001 | B1 |
6171547 | Sagara et al. | Jan 2001 | B1 |
6235237 | Osing et al. | May 2001 | B1 |
6294131 | Jaffrey | Sep 2001 | B1 |
6352670 | Rakowski | Mar 2002 | B1 |
6379476 | Tarutani et al. | Apr 2002 | B1 |
6409847 | Kleemann | Jun 2002 | B2 |
6423159 | Liesert et al. | Jul 2002 | B1 |
6426039 | Hirasawa et al. | Jul 2002 | B2 |
6440236 | Hiramatsu et al. | Aug 2002 | B1 |
6440579 | Hauser et al. | Aug 2002 | B1 |
6485680 | Ragot et al. | Nov 2002 | B2 |
6500280 | Ota et al. | Dec 2002 | B2 |
6521056 | Muraki et al. | Feb 2003 | B2 |
6547891 | Linden et al. | Apr 2003 | B2 |
6551420 | Bergstrom et al. | Apr 2003 | B1 |
6564990 | Nagashima et al. | May 2003 | B2 |
6582835 | Antoni et al. | Jun 2003 | B2 |
6592685 | Goecmen | Jul 2003 | B2 |
6623569 | Bergstrom et al. | Sep 2003 | B2 |
6645324 | Hirata et al. | Nov 2003 | B2 |
6673165 | Koga et al. | Jan 2004 | B2 |
6673166 | Oku et al. | Jan 2004 | B2 |
6682582 | Speidel | Jan 2004 | B1 |
6682780 | Tzatzov et al. | Jan 2004 | B2 |
6692592 | Kidani et al. | Feb 2004 | B2 |
6696016 | Kimura | Feb 2004 | B1 |
6723181 | Ishikawa et al. | Apr 2004 | B2 |
6740174 | Miyazaki et al. | May 2004 | B2 |
6793744 | Jung | Sep 2004 | B1 |
6793746 | Shimizu et al. | Sep 2004 | B2 |
6855213 | Yoshitake et al. | Feb 2005 | B2 |
6921440 | Liesert et al. | Jul 2005 | B2 |
7081173 | Bahar et al. | Jul 2006 | B2 |
7094295 | Oku et al. | Aug 2006 | B2 |
7166174 | De Bondt et al. | Jan 2007 | B2 |
7255755 | Maziasz et al. | Aug 2007 | B2 |
7335428 | Fraisse et al. | Feb 2008 | B2 |
7341690 | Miyazaki et al. | Mar 2008 | B2 |
7343730 | Humcke et al. | Mar 2008 | B2 |
7476282 | Tanida et al. | Jan 2009 | B2 |
7531129 | Igarashi et al. | May 2009 | B2 |
7572407 | Hirasawa et al. | Aug 2009 | B2 |
7731895 | Okada et al. | Jun 2010 | B2 |
7749431 | Igarashi et al. | Jul 2010 | B2 |
RE41504 | Maziasz et al. | Aug 2010 | E |
7767037 | Kimura et al. | Aug 2010 | B2 |
7780798 | Stinson et al. | Aug 2010 | B2 |
7819991 | Kato et al. | Oct 2010 | B2 |
7842141 | Kimura et al. | Nov 2010 | B2 |
7923126 | Gudme | Apr 2011 | B2 |
7981561 | Rakowski et al. | Jul 2011 | B2 |
8025839 | Jonson et al. | Sep 2011 | B2 |
8062584 | Hamada et al. | Nov 2011 | B2 |
8152937 | Ishii et al. | Apr 2012 | B2 |
8153055 | Nakamura et al. | Apr 2012 | B2 |
8226780 | Hatano et al. | Jul 2012 | B2 |
8268101 | Conrad et al. | Sep 2012 | B2 |
8287805 | Sjodin | Oct 2012 | B2 |
8303733 | Hamada et al. | Nov 2012 | B2 |
8333849 | Yamauchi et al. | Dec 2012 | B2 |
8333851 | Suwabe | Dec 2012 | B2 |
8337748 | Rakowski et al. | Dec 2012 | B2 |
8337749 | Bergstrom et al. | Dec 2012 | B2 |
8357247 | Hirasawa et al. | Jan 2013 | B2 |
8506727 | Pelsoeczy | Aug 2013 | B2 |
8535606 | John | Sep 2013 | B2 |
8540933 | Nylof et al. | Sep 2013 | B2 |
8562758 | Fujisawa et al. | Oct 2013 | B2 |
8580048 | Pelsoeczy | Nov 2013 | B2 |
8608873 | Abratis et al. | Dec 2013 | B2 |
8663549 | Ohishi et al. | Mar 2014 | B2 |
8721960 | Hatano et al. | May 2014 | B2 |
8790573 | Miyazaki et al. | Jul 2014 | B2 |
8877121 | Bergstrom et al. | Nov 2014 | B2 |
8894924 | Matsuhashi et al. | Nov 2014 | B2 |
8980167 | Kimura et al. | Mar 2015 | B2 |
9150947 | Nishiyama et al. | Oct 2015 | B2 |
9181824 | Montagnon | Nov 2015 | B2 |
9279172 | Kato et al. | Mar 2016 | B2 |
9290845 | Kim et al. | Mar 2016 | B2 |
20020033210 | Fujitsuna et al. | Mar 2002 | A1 |
20030086810 | Schnabel et al. | May 2003 | A1 |
20030172999 | Alfonsson et al. | Sep 2003 | A1 |
20040040631 | Takahashi et al. | Mar 2004 | A1 |
20040050462 | Grubb | Mar 2004 | A1 |
20040074574 | Kimura | Apr 2004 | A1 |
20040156737 | Rakowski | Aug 2004 | A1 |
20040166015 | Kimura | Aug 2004 | A1 |
20040244884 | Hideshima et al. | Dec 2004 | A1 |
20050139298 | Pacher et al. | Jun 2005 | A1 |
20050217769 | Pacher et al. | Oct 2005 | A1 |
20050269074 | Chitwood | Dec 2005 | A1 |
20060008694 | Budinski et al. | Jan 2006 | A1 |
20060150388 | Inada et al. | Jul 2006 | A1 |
20060266439 | Maziasz et al. | Nov 2006 | A1 |
20060285989 | Schade | Dec 2006 | A1 |
20070089810 | Sundstrom et al. | Apr 2007 | A1 |
20070187002 | Takahashi et al. | Aug 2007 | A1 |
20080073004 | Pacher et al. | Mar 2008 | A1 |
20080206088 | Cusolito et al. | Aug 2008 | A1 |
20090032246 | Takabe et al. | Feb 2009 | A1 |
20090053093 | Oku et al. | Feb 2009 | A1 |
20090060775 | Liu | Mar 2009 | A1 |
20090111607 | Taylor et al. | Apr 2009 | A1 |
20090324441 | Weiss et al. | Dec 2009 | A1 |
20100000636 | Bonnefois et al. | Jan 2010 | A1 |
20100133096 | Hansen et al. | Jun 2010 | A1 |
20100183475 | Radon et al. | Jul 2010 | A1 |
20100189589 | Liu | Jul 2010 | A1 |
20100223927 | Oku et al. | Sep 2010 | A1 |
20100272593 | Ishikawa et al. | Oct 2010 | A1 |
20110061777 | Ishii et al. | Mar 2011 | A1 |
Number | Date | Country |
---|---|---|
2707518 | Jul 2009 | CA |
2762899 | Dec 2010 | CA |
2860746 | Aug 2013 | CA |
86101805 | Aug 1986 | CN |
101680066 | Mar 2010 | CN |
101784686 | Jul 2010 | CN |
0547626 | Jun 1993 | EP |
0638653 | Feb 1995 | EP |
S56-146857 | Nov 1981 | JP |
S58-39732 | Mar 1983 | JP |
S60-2622 | Jan 1985 | JP |
H04-280948 | Oct 1992 | JP |
H08-199314 | Aug 1996 | JP |
H08 246105 | Sep 1996 | JP |
H08 311543 | Nov 1996 | JP |
H09 227999 | Sep 1997 | JP |
H09 228002 | Sep 1997 | JP |
H10 81940 | Mar 1998 | JP |
2006-097908 | Apr 2006 | JP |
2006-131945 | May 2006 | JP |
2006-257544 | Sep 2006 | JP |
2007-131870 | May 2007 | JP |
2007-302995 | Nov 2007 | JP |
2008-291303 | Dec 2008 | JP |
2009-035813 | Feb 2009 | JP |
2010-202916 | Sep 2010 | JP |
2010-202973 | Sep 2010 | JP |
2011-179116 | Sep 2011 | JP |
2132886 | Jul 1999 | RU |
2242325 | Dec 2004 | RU |
2429306 | Sep 2011 | RU |
I482866 | May 2015 | TW |
111115 | Mar 2016 | UA |
WO 2008156195 | Dec 2008 | WO |
Entry |
---|
“JFE443CT, Ni, Mo-free stainless steel with high corrosion resistance: 21Cr Stainless Steel,” JFE Steel Corporation, Catalog No. G1E-004-01, 2006. |
International Search Report and Written Opinion dated Jul. 24, 2013 for Application No. PCT/US2013/034940. |
English Abstract of Japanese Patent No. JP H08 246105. |
English Abstract of Japanese Patent No. JP H08 311543. |
English Abstract of Japanese Patent No. JP H09 227999. |
English Abstract of Japanese Patent No. JP H09 228002. |
English Abstract of Japanese Patent No. JP H10 91940. |
“JFE443CT, Ni, Mo-free stainless steel with high corrosion resistance: 21Cr Stainless Steel,” JFE Steel Corporation, Catalog No. G1E-004-03, 2012, accessed from: http://www.jfe-steel.co.jp/en/products/stainless/catalog/gle-004.pdf. |
Canadian Office Action dated Jan. 22, 2016 for Application No. CA 2,868,278, 6 pgs. |
Chinese Office Action dated Sep. 18, 2015 for Application No. CN 201380018563.7, 8 pgs. |
European Exam Report dated Sep. 1, 2015 for Application No. EP 13716682.3, 5 pgs. |
Japanese Office Action dated Nov. 10, 2015 for Application No. JP 2015-504675, 9 pgs. |
Korean Office Action dated Oct. 12, 2015 for Application No. KR 10-2014-7030826, 5 pgs. |
Russian Office Action dated Apr. 8, 2016 for Application No. RU 2014138182/02(061887), 14 pgs. |
Taiwanese Search Report dated Jun. 23, 2014 for Application No. TW 102111957, 6 pgs. |
Ukrainian Office Action dated Dec. 12, 2014 for Application No. UA a 2014 10374, 4 pgs. |
Korean Office Action, Notice of Final Rejection, dated Feb. 16, 2017 for Application No. 10-2014-7030826, 6 pages. |
Australian Office Action dated Oct. 6, 2016 for Application No. 2013243635, 3 pages. |
Canadian Office Action dated Nov. 23, 2016 for Application No. 2,868,278, 3 pages. |
Chinese Office Action dated May 10, 2016 for Application No. 201380018563.7, 8 pages. |
Chinese Office Action dated Dec. 8, 2016 for Application No. 201380018563.7, 11 pages. |
Japanese Office Action, Examiner's Decision of Refusal, dated Aug. 16, 2016 for Application No. 2015-504675, 8 pages. |
Korean Office Action, Notice of Final Rejection, dated Jun. 20, 2016 for Application No. 10-2014-7030826, 6 pages. |
Korean Office Action, Notice of Preliminary Rejection, dated Sep. 27, 2016 for Application No. 10-2014-7030826, 7 pages. |
Russian Office Action, Notice of Allowance, dated Jul. 8, 2016 for Application No. 2014138182/02, 13 pages. |
Number | Date | Country | |
---|---|---|---|
20130294960 A1 | Nov 2013 | US |
Number | Date | Country | |
---|---|---|---|
61619048 | Apr 2012 | US |