EP1563104B1 - Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech - Google Patents

Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech Download PDF

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EP1563104B1
EP1563104B1 EP03782551A EP03782551A EP1563104B1 EP 1563104 B1 EP1563104 B1 EP 1563104B1 EP 03782551 A EP03782551 A EP 03782551A EP 03782551 A EP03782551 A EP 03782551A EP 1563104 B1 EP1563104 B1 EP 1563104B1
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plate
optionally
process according
steel
titanium
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EP1563104A1 (de
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Jean Beguinot
Jean-Georges Brisson
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Industeel Creusot
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Industeel Creusot
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18Hardening; Quenching with or without subsequent tempering
    • C21D1/19Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/001Austenite
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/002Bainite
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00Microstructure comprising significant phases
    • C21D2211/008Martensite
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the present invention relates to an abrasion-resistant steel and its method of manufacture.
  • Abrasion resistant steels are well known and are generally steels of high hardness (between 400 and 500 Brinell) having a martensitic structure, and containing from 0.12% to 0.3% carbon. It is generally accepted that in order to increase the wear resistance it is sufficient to increase the hardness, but this is done to the detriment of other properties such as the ability to weld or shape by folding, for example . Also, in order to obtain steels having both very good wear resistance and good processability, other means have been sought besides increasing the hardness.
  • the object of the present invention is to overcome these disadvantages by providing an abrasion-resistant steel sheet having a good flatness and which, all things being equal, has an abrasion resistance better than that of steels. known.
  • quenching may be followed by tempering at a temperature below 350 ° C, and preferably below 250 ° C.
  • the invention also relates to a part, and in particular a sheet obtained in particular by this method, the steel having a structure consisting of 5% to 20% retained austenite, the remainder of the structure being martensitic or martensite-bainitic with carbides .
  • the piece is a sheet, its thickness may be between 2 mm and 150 mm and its flatness may be characterized by an arrow less than or equal to 12 mm / m, and preferably less than 5 mm / m.
  • the hardness is preferably between 280 HB and 450 HB.
  • the hardness is preferably between 380 HB and 550 HB.
  • the hardness is preferably between 450 HB and 650 HB.
  • the carbon, titanium, zirconium and nitrogen contents must be such that: 0 , 1 % ⁇ VS - Ti / 4 - Zr / 8 + 7 ⁇ NOT / 8 ⁇ 0 , 55 %
  • C * represents the free carbon content after precipitation of the titanium and zirconium carbides, taking into account the formation of titanium and zirconium nitrides.
  • This free carbon content C * must be greater than 0.1%, and preferably greater than or equal to 0.22%, to have a martensite having a minimum hardness, but beyond 0.55% the toughness and the the processability are too deteriorated.
  • the chemical composition must be chosen so that the quenchability of the steel is sufficient, given the thickness of the sheet that is to be manufactured.
  • the silicon content is greater than 0.5% so as to promote the formation of retained austenite.
  • the contents of Ti, Zr and N should preferably be such that: Ti + Zr / 2 - 7xN / 2 ⁇ 0.05%, and more preferably greater than 0.1%, and more preferably, greater than 0.3% for the carbide content to be sufficient.
  • the micrographic structure of the steel consists of martensite or bainite or a mixture of these two structures, and from 5% to 20% retained austenite.
  • This structure further comprising large titanium or zirconium carbides, or even carbides of niobium, tantalum or vanadium, formed at high temperature.
  • the inventors have found that the effectiveness of large carbides for the improvement of the abrasion resistance could be obelated by premature loosening thereof and that this loosening could be avoided by the presence of metastable austenite which is transformed in fresh martensite under the effect of abrasion phenomena.
  • the conversion of the metastable austenite to fresh martensite is by swelling, this transformation in the abraded underlayer increases the resistance to carburetion and thus improves the abrasion resistance.
  • the steel is made, it flows in the form of slab or ingot.
  • the slab or slug is hot-rolled to obtain a sheet which is subjected to a heat treatment which makes it possible at the same time to obtain the desired structure and a good flatness without subsequent planing or with limited planing.
  • the heat treatment can be carried out directly in the hot rolling or carried out later, possibly after a cold planing or half-hot.
  • an expansion treatment can be carried out at a temperature of less than or equal to 350 ° C, and preferably less than or equal to 250 ° C.
  • the hardness being a function of the free carbon content C * the same hardness can be obtained with very different titanium or zirconium contents. With equal hardness, the resistance to abrasion is all the higher as the titanium or zirconium content is important. Similarly, titanium content or equal zirconium, the resistance to abrasion is even better than the hardness is high. In addition, the implementation of the steel is all the easier as the free carbon content is low, but with equal free carbon content, ductility is even better than the titanium content is low. All of these considerations make it possible to choose the carbon and titanium or zirconium contents which lead to all of the properties best suited to each field of application.
  • steel sheets identified A to G according to the invention and H to J according to the prior art are considered.
  • the chemical compositions of the steels, expressed in 10 -3 % by weight, as well as the hardness, the residual austenite content of the structure and a wear resistance index Rus, are reported in Table 1.
  • the wear resistance index Rus varies as the logarithm of the inverse of the weight loss of a prismatic specimen rotated in a tank containing calibrated quartzite granules.
  • All the sheets have a thickness of 30 mm, and the sheets corresponding to the steels A to G have been quenched according to the invention, after austenitization at 900 ° C.
  • the sheets according to the invention have a martensite-bainitic structure containing from 5% to 20% retained austenite, whereas the sheets given for comparison have a completely martensitic structure, that is to say, martensitic and not containing more than 2 or 3% retained austenite. All plates contain carbides.
  • the pair of steels F, G (according to the invention) is clearly different from the pair of steels I, J, term of gain of holding brought by the titanium.
  • the resistance gain Rus supplied by 0.245% of Ti is 0.46, whereas it is only 0.31 for a difference of 0.265% of Ti in the case of the pair I, J. .
  • the deformation after cooling, without planing, for the steel sheets according to the invention is less than 10 mm / m, and is about 15 mm / m for the steel sheet H.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Articles (AREA)
  • Soft Magnetic Materials (AREA)

Claims (20)

  1. Verfahren zur Herstellung eines Gegenstands, beispielsweise eines Blechs, aus abriebfestem Stahl, dessen chemische Zusammensetzung gewichtsbezogen Folgendes umfasst: 0 , 35 % C 0 , 8 %
    Figure imgb0129
    0 % Si 2 %
    Figure imgb0130
    0 % Al 2 %
    Figure imgb0131
    0 , 35 % Si + Al 2 %
    Figure imgb0132
    0 % Mn 2 , 5 %
    Figure imgb0133
    0 % Ni 5 %
    Figure imgb0134
    0 % Cr 5 %
    Figure imgb0135
    0 % Mo 0 , 5 %
    Figure imgb0136
    0 % W 1 , 00 %
    Figure imgb0137
    0 , 1 % Mo + W / 2 0 , 50 %
    Figure imgb0138
    0 % B 0 , 02 %
    Figure imgb0139
    0 % Ti 2 %
    Figure imgb0140
    0 % Zr 4 %
    Figure imgb0141
    0 , 05 % Ti + Zr / 2 2 %
    Figure imgb0142
    0 % S 0 , 15 %
    Figure imgb0143
    N < 0 , 03 %
    Figure imgb0144
    - gegebenenfalls 0 % bis 1,5 % Kupfer,
    - gegebenenfalls mindestens ein aus Nb, Ta und V ausgewähltes Element in derartigen Anteilen, dass Nb/2 + Ta/4 + V ≤ 0,5 % gilt,
    - gegebenenfalls mindestens ein aus Se, Te, Ca, Bi und Pb ausgewähltes Element in Anteilen von weniger als oder gleich 0,1 %,
    wobei der Rest Eisen oder Verunreinigungen, die sich aus der Erzeugung ergeben, sind und die chemische Zusammensetzung ferner den folgenden Gleichungen genügt: 0 , 1 % C - Ti / 4 - Zr / 8 + 7 × N / 8 0 , 55 %
    Figure imgb0145
    und: Ti + Zr / 2 - 7 × N / 2 0 , 05 %
    Figure imgb0146
    und: 1 , 05 × Mn + 0 , 54 × Ni + 0 , 50 × Cr + 0 , 3 × ( Mo + W / 2 ) 1 / 2 + K > 1 , 8 ,
    Figure imgb0147

    worin K = 0,5 wenn B ≥ 0,0005 % und K = 0 wenn B < 0,0005 % gilt,
    demzufolge der Gegenstand oder das Blech einer Wärmebehandlung zum Härten unterzogen wird, die in der Hitze der Warmformgebung und beispielsweise in der Walzhitze oder nach der Austenitisierung durch Erhitzen in einem Ofen durchgeführt wird, wobei zum Härten:
    - der Gegenstand oder das Blech mit einer mittleren Abkühlungsgeschwindigkeit von über 0,5 °C/s zwischen einer Temperatur von über AC3 und einer Temperatur zwischen T = 800 - 270 x C* - 90 x Mn - 37 x Ni - 70 X Cr - 83 x (Mo + W/2), worin C* = C - Ti/4 - Zr/8 + 7 x N/8 gilt, und T - 50 °C abgekühlt wird,
    - anschließend der Gegenstand oder das Blech mit einer Kernabkühlungsgeschwindigkeit Vr < 1150 x ep-1,7 und über 0,1 °C/s zwischen der Temperatur T und 100 °C abgekühlt wird, wobei ep die Dicke des Gegenstands oder des Blechs in mm ist,
    - der Gegenstand oder das Blech auf die Umgebungstemperatur abgekühlt wird und gegebenenfalls eine Glättung durchgeführt wird.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, dass: 1 , 05 × Mn + 0 , 54 × Ni + 0 , 50 × Cr + 0 , 3 × ( Mo + W / 2 ) 1 / 2 + K > 2
    Figure imgb0148
    gilt.
  3. Verfahren nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass: C > 0 , 45 %
    Figure imgb0149
    gilt.
  4. Verfahren nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass: Si + Al > 0 , 5 %
    Figure imgb0150
    gilt.
  5. Verfahren nach einem der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass: Ti + Zr / 2 > 0 , 10 %
    Figure imgb0151
    gilt.
  6. Verfahren nach einem der Ansprüche 1 bis 5,
    dadurch gekennzeichnet, dass: Ti + Zr / 2 > 0 , 30 %
    Figure imgb0152
    gilt.
  7. Verfahren nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass C * 0 , 22 %
    Figure imgb0153
    gilt.
  8. Verfahren nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass ferner ein Anlassen bei einer Temperatur von unter oder gleich 350 °C durchgeführt wird.
  9. Verfahren nach einem der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass zum Zusetzen von Titan zum Stahl der flüssige Stahl in Kontakt mit einer titanhaltigen Schlacke gebracht wird und das Titan der Schlacke langsam in den flüssigen Stahl eindiffundieren gelassen wird.
  10. Gegenstand, insbesondere ein Blech, aus abriebfestem Stahl, dessen chemische Zusammensetzung gewichtsbezogen Folgendes umfasst: 0 , 35 % C 0 , 8 %
    Figure imgb0154
    0 % Si 2 %
    Figure imgb0155
    0 % Al 2 %
    Figure imgb0156
    0 , 35 % Si + Al 2 %
    Figure imgb0157
    0 % Mn 2 , 5 %
    Figure imgb0158
    0 % Ni 5 %
    Figure imgb0159
    0 % Cr 5 %
    Figure imgb0160
    0 % Mo 0 , 50 %
    Figure imgb0161
    0 % W 1 , 00 %
    Figure imgb0162
    0 , 1 % Mo + W / 2 0 , 50 %
    Figure imgb0163
    0 % B 0 , 02 %
    Figure imgb0164
    0 % Ti 2 %
    Figure imgb0165
    0 % Zr 4 %
    Figure imgb0166
    0 , 05 % Ti + Zr / 2 2 %
    Figure imgb0167
    0 % S 0 , 15 %
    Figure imgb0168
    N < 0 , 03 %
    Figure imgb0169
    - gegebenenfalls 0 % bis 1,5 % Kupfer,
    - gegebenenfalls mindestens ein aus Nb, Ta und V ausgewähltes Element in derartigen Anteilen, dass Nb/2 + Ta/4 + V ≤ 0,5 % gilt,
    - gegebenenfalls mindestens ein aus Se, Te, Ca, Bi und Pb ausgewähltes Element in Anteilen von weniger als oder gleich 0,1 %,
    wobei der Rest Eisen oder Verunreinigungen, die sich aus der Erzeugung ergeben, sind und die chemische Zusammensetzung ferner den folgenden Gleichungen genügt: 0 , 1 % C - Ti / 4 - Zr / 8 + 7 × N / 8 0 , 55 %
    Figure imgb0170
    und: Ti + Zr / 2 - 7 × N / 2 0 , 05 %
    Figure imgb0171
    und: 1 , 05 × Mn + 0 , 54 × Ni + 0 , 50 × Cr + 0 , 3 × ( Mo + W / 2 ) 1 / 2 + K > 1 , 8 ,
    Figure imgb0172

    worin K = 0,5 wenn B ≥ 0,0005 % und K = 0 wenn B < 0,0005 % gilt,
    wobei die Ebenheit durch eine Durchbiegung von unter 12 mm/m gekennzeichnet ist und der Stahl ein Martensitgefüge oder ein Martensit-Bainit-Gefüge aufweist, wobei das Gefüge ferner 5 % bis 20 % Restaustenit und Carbide enthält.
  11. Gegenstand nach Anspruch 10, dadurch gekennzeichnet, dass: 1 , 05 × Mn + 0 , 54 × Ni + 0 , 50 × Cr + 0 , 3 × ( Mo + W / 2 ) 1 / 2 + K > 2
    Figure imgb0173
    gilt.
  12. Gegenstand nach Anspruch 10 oder 11, dadurch gekennzeichnet, dass: C > 0 , 45 %
    Figure imgb0174
    gilt.
  13. Gegenstand nach einem der Ansprüche 10 bis 12, dadurch gekennzeichnet, dass: Si + Al > 0 , 5 %
    Figure imgb0175
    gilt.
  14. Gegenstand nach einem der Ansprüche 10 bis 13, dadurch gekennzeichnet, dass: Ti + Zr / 2 > 0 , 10 %
    Figure imgb0176
    gilt.
  15. Gegenstand nach einem der Ansprüche 10 bis 14, dadurch gekennzeichnet, dass: Ti + Zr / 2 > 0 , 30 %
    Figure imgb0177
    gilt.
  16. Gegenstand nach einem der Ansprüche 10 bis 15, dadurch gekennzeichnet, dass: C * 0 , 22 %
    Figure imgb0178
    gilt.
  17. Gegenstand nach einem der Ansprüche 10 bis 16, dadurch gekennzeichnet, dass die Dicke des Blechs zwischen 2 mm und 150 mm beträgt und seine Ebenheit durch eine Durchbiegung von unter 12 mm/m gekennzeichnet ist.
  18. Gegenstand nach einem der Ansprüche 10 bis 17, dadurch gekennzeichnet, dass die Härte zwischen 280 HB und 450 HB beträgt und: 0 , 1 % C - Ti / 4 - Zr / 8 + 7 × N / 8 0 , 2 %
    Figure imgb0179
    gilt.
  19. Gegenstand nach einem der Ansprüche 10 bis 17, dadurch gekennzeichnet, dass die Härte zwischen 380 HB und 550 HB beträgt und: 0 , 2 % < C - Ti / 4 - Zr / 8 + 7 × N / 8 0 , 3 %
    Figure imgb0180
    gilt.
  20. Gegenstand nach einem der Ansprüche 10 bis 17, dadurch gekennzeichnet, dass die Härte zwischen 450 HB und 650 HB beträgt und: 0 , 3 % < C - Ti / 4 - Zr / 8 + 7 × N / 8 0 , 5 %
    Figure imgb0181
    gilt.
EP03782551A 2002-11-19 2003-11-13 Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech Expired - Lifetime EP1563104B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
SI200331362T SI1563104T1 (sl) 2002-11-19 2003-11-13 Postopek za izdelavo abrazijsko odporne jeklene pločevine in tako izdelana pločevina

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Application Number Priority Date Filing Date Title
FR0214424A FR2847270B1 (fr) 2002-11-19 2002-11-19 Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR0214424 2002-11-19
PCT/FR2003/003359 WO2004048620A1 (fr) 2002-11-19 2003-11-13 Procede pour fabriquer une tole en acier resistant a l'abrasion et tôle obtenue

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EP1563104B1 true EP1563104B1 (de) 2008-07-09

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US (3) US7459041B2 (de)
EP (1) EP1563104B1 (de)
JP (1) JP4535877B2 (de)
KR (1) KR101010570B1 (de)
CN (1) CN100350061C (de)
AR (1) AR042071A1 (de)
AT (1) ATE400667T1 (de)
AU (1) AU2003290188B2 (de)
BR (2) BR122013002046B8 (de)
CA (1) CA2506351C (de)
DE (1) DE60322092D1 (de)
ES (1) ES2309377T3 (de)
FR (1) FR2847270B1 (de)
PE (1) PE20040487A1 (de)
PL (1) PL204080B1 (de)
RU (1) RU2327802C2 (de)
SI (1) SI1563104T1 (de)
UA (1) UA80308C2 (de)
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FR2847274B1 (fr) * 2002-11-19 2005-08-19 Usinor Piece d'acier de construction soudable et procede de fabrication
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ATE400667T1 (de) 2008-07-15
EP1563104A1 (de) 2005-08-17
FR2847270B1 (fr) 2004-12-24
BR0315697B1 (pt) 2013-07-30
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CA2506351A1 (fr) 2004-06-10
US20080253920A1 (en) 2008-10-16
KR101010570B1 (ko) 2011-01-25
ZA200504005B (en) 2006-07-26
ES2309377T3 (es) 2008-12-16
BR122013002046B1 (pt) 2017-04-25
KR20050083913A (ko) 2005-08-26
PL375544A1 (en) 2005-11-28
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RU2327802C2 (ru) 2008-06-27
JP2006506528A (ja) 2006-02-23
US20080247903A1 (en) 2008-10-09
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UA80308C2 (en) 2007-09-10
US20060137780A1 (en) 2006-06-29
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US8709336B2 (en) 2014-04-29
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