EP3099832B1 - Laiton présentant une meilleure résistance à la dézincification et une meilleure usinabilité - Google Patents

Laiton présentant une meilleure résistance à la dézincification et une meilleure usinabilité Download PDF

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Publication number
EP3099832B1
EP3099832B1 EP15709371.7A EP15709371A EP3099832B1 EP 3099832 B1 EP3099832 B1 EP 3099832B1 EP 15709371 A EP15709371 A EP 15709371A EP 3099832 B1 EP3099832 B1 EP 3099832B1
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Prior art keywords
weight
brass alloy
alloy
brass
phase
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EP15709371.7A
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German (de)
English (en)
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EP3099832A2 (fr
Inventor
Jan Nilsson
Cato MARTINSEN MERELID
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Nordic Brass Gusum AB
IMI Hydronic Engineering AB
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Nordic Brass Gusum AB
IMI Hydronic Engineering AB
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/005—Castings of light metals with high melting point, e.g. Be 1280 degrees C, Ti 1725 degrees C
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon

Definitions

  • the present invention concerns an essentially arsenic-free brass alloy with improved dezincification resistance, protection against intergranular grain boundary corrosion, and machinability.
  • Brass is a material the basic components of which are copper (Cu) and zinc (Zn).
  • alloying materials such as lead (Pb), iron (Fe), aluminium (Al), nickel (Ni), manganese (Mn), silicon (Si)
  • the brass can be given unique properties, and there are many different brass alloys adapted to different types of processing and final products.
  • the brass will consist of different so-called phases, which are microstructure components.
  • the usual phases of brass are the ⁇ -phase, which is rich in copper and the ⁇ -phase, which is rich in zinc. Often, brass consists of a mixture of these two phases.
  • a solid solution having a uniform brass composition is formed when up to about 35 % by weight of zinc is added to copper.
  • a further increase of the content of zinc gives a mixture of the original solid solution (the ⁇ -phase) and a new solid solution having a higher content of zinc (the ⁇ -phase).
  • Brass containing between 35-45 % by weight of zinc consists of mixtures of these two phases and is called ⁇ - ⁇ -brass or duplex brass, the relationship between the ⁇ -phase to the ⁇ -phase depending primarily on the content of zinc.
  • the presence of ⁇ -phase in ⁇ - ⁇ -brass gives a decreased cold ductility but a considerably increased susceptibility to hot working by extrusion or punching and casting without thermal cracks, also when lead is present.
  • ⁇ - ⁇ -alloys have better mechanical properties and, since they contain a higher share of zinc, they are in certain cases more inexpensive than ⁇ -brass.
  • ⁇ - ⁇ -brass alloys have a higher sensitivity to dezincification. Thereby, there is a need of producing ⁇ - ⁇ -brass alloys with dezincification resistance.
  • Dezincification is a type of corrosion where zinc selectively is attacked and leaves a porous copper structure.
  • Dezincification resistant brass has a relatively high Cu content, above 60 %, and contains an inhibitor such arsenic (As), antimony (Sb), or phosphorus (P), which makes the ⁇ -phase of the brass resistant to dezincification. Since only the ⁇ -phase can be stabilized, it is important to minimize the content of ⁇ -phase by a higher content of copper.
  • Brass alloys may in addition to dezincification be subjected to intergranular grain boundary corrosion, which is a form of corrosion taking place along the grain boundaries.
  • intergranular grain boundary corrosion is a form of corrosion taking place along the grain boundaries.
  • the content of zinc is higher at the grain boundaries of brass alloys and intergranular grain boundary corrosion attacks just at the zinc present along the grain boundaries. Thereby, there is also a need of protecting brass alloys against intergranular grain boundary corrosion.
  • the American Academy of Sciences has estimated the lifetime risk of cancer to 1-3 cases per 1000 individuals at a daily intake of 1 l of drinking water having arsenic contents at the threshold level of 10 ⁇ g/l, which exceeds the low-risk level (approx. one case per 100 000 exposed) that could be considered to be an acceptable risk of an individual environmental factor [3]. As with other carcinogenic substances, the risk of health effects decreases at decreased exposure.
  • the threshold for arsenic in drinking water is 10 ⁇ g/l within the EU.
  • the threshold for arsenic in drinking water in Sweden 10 ⁇ g/l, is based on the cancer risk [3].
  • Lifetime risk of the genesis of cancer at a daily intake of arsenic corresponding to the threshold in drinking water (10-20 ⁇ g arsenic per day depending on age, climate and physical activity), has been estimated to 1-3 per 1 000 individuals (0.1-0.3 %). Thereby, it is desirable to limit the intake of arsenic as far as possible. This applies particularly to children, since experimental studies show that foetuses and small children are more sensible than adults.
  • the object of the present invention is to provide an essentially arsenic-free ⁇ - ⁇ -brass alloy.
  • the object is furthermore that the brass alloy has improved dezincification resistance than brass alloys with arsenic or solely arsenic.
  • the object is furthermore to provide a brass alloy having similar or better protection against intergranular grain boundary corrosion than brass alloys with arsenic or solely arsenic.
  • the object is furthermore that the lead content of the brass alloy should be ⁇ 1.0 % by weight, preferably ⁇ 0.10 % by weight of Pb.
  • the object is furthermore that the content of the ⁇ -phase is ⁇ 5 %, preferably ⁇ 1 %.
  • the invention concerns an essentially arsenic-free ⁇ - ⁇ -brass alloy with improved (i) dezincification resistance, (ii) machinability, and (iii) protection against intergranular grain boundary corrosion.
  • the essentially arsenic-free brass alloy comprises 62-68 % by weight of Cu, 0.02-1.00 % by weight of Pb, ⁇ 0.02 % by weight of As, and/or 0.01-0.06 % by weight of P and/or 0.01-0.06 % by weight of Sb (antimony), and balance Zn.
  • Said brass alloy is characterized in that it comprises ⁇ 5 % of ⁇ -phase, preferably ⁇ 1 %. Since only the ⁇ -phase can be stabilized, it is important to minimize the content of ⁇ -phase to ⁇ 5 % of ⁇ -phase, preferably ⁇ 1 %, with the purpose of counteracting dezincification and intergranular grain boundary corrosion.
  • the essentially arsenic-free brass alloy comprises 62-68 % by weight of Cu, 0.02-1.00 % by weight of Pb, ⁇ 0.02 % by weight of As, and/or 0.01-0.06 % by weight of P and/or 0.01-0.06 % by weight of Sb, and balance Zn, the brass alloy being produced by means of a method comprising the steps of:
  • the essentially arsenic-free brass alloy has been characterized by the method of producing it (product-by-process) in combination with other determinations of the alloy since it is difficult to define the technical features of the alloy in another way, i.e., it is partly thanks to heat treatment that the alloy obtains improved (i) dezincification resistance and (ii) protection against intergranular grain boundary corrosion.
  • the essentially arsenic-free brass alloy comprises 63.0-64.0 % by weight of Cu, 0.02-1.00 % by weight of Pb, and/or 0.02-0.06 % by weight of P, 0.02-0.06 % by weight of Sb, and balance Zn.
  • the somewhat higher amount of Pb gives a certain improved machinability.
  • the essentially arsenic-free brass alloy comprises 63.0-64.0 % by weight of Cu, 0.80-1.00 % by weight of Pb, 0.02-0.06 % by weight of P, 0.02-0.06 % by weight of Sb, and balance Zn.
  • the somewhat higher amount of Pb gives a certain improved machinability.
  • the essentially arsenic-free brass alloy comprises also 0.07-0.12 % by weight of Fe and 0-0.05 % by weight or 0.45-0.70 % by weight of Al.
  • the presence of Fe and Al in the brass alloy entails a certain increased hardness, strength, and tensile strength.
  • the essentially arsenic-free brass alloy comprises 63.5 % by weight of Cu, 35.0 % by weight of Zn, 0.9 % by weight of Pb, 0.10 % by weight of Fe, 0.50 % by weight of Al, 0.02-0.06 % by weight of P, 0.02-0.06 % by weight of Sb. Alloying additives such as Fe and Al improve strength, hardness, and tensile strength. The content of P and Sb of 0.02-0.06 % by weight each gives protection against dezincification and intergranular grain boundary corrosion.
  • the essentially arsenic-free brass alloy comprises 63.5 % by weight of Cu, 35.0 % by weight of Zn, 0.9 % by weight of Pb, 0.10 % by weight of Fe, 0.50 % by weight of Al, 0.03 % by weight of P, and 0.03 % by weight of Sb.
  • the content of P and Sb of 0.03 % by weight each gives better protection against dezincification and intergranular grain boundary corrosion and approx. 10 % lower cutting forces.
  • the essentially arsenic-free brass alloy comprises 0-0.200 % by weight of Ni, 0-0.100 % by weight of Mn, 0-0.02 % by weight of Si, 0-0.002 % by weight of As and/or 0.0004-0.0006 % by weight of B (boron), preferably 0.0005 % by weight of B.
  • Nickel improves corrosion resistance, hardness, and tensile strength without significant effect on ductility, which gives improved properties at elevated temperatures.
  • Mn entails a certain increased hardness, strength, and tensile strength.
  • Si increases the strength, workability, and the resistance to wear.
  • the content of As and B is acceptable contents of inevitable impurities in the alloy.
  • the brass alloy comprises 62-68 % by weight of Cu, 0.02-1.00 % by weight of Pb, 0.01 % by weight of As, 0.02 % by weight of Sb, and balance Zn.
  • the brass alloy comprises 62-68 % by weight of Cu, 0.02-1.00 % by weight of Pb, 0.01 % by weight of As, 0.02 % by weight of Sb, 0.015 % by weight of P, and balance Zn.
  • the essentially arsenic-free brass alloy according to the present application is produced by the steps of:
  • the essentially arsenic-free brass alloy is produced by heat treating at 550 °C for 2 h, which lowers the amount of ⁇ -phase to ⁇ 5 %, preferably ⁇ 1 %, as well as that the alloying additive P lowers the cutting forces to approx. 10 % lower cutting forces.
  • the present invention concerns an essentially arsenic-free brass alloy with improved (i) dezincification resistance, (ii) machinability, and (iii) protection against intergranular grain boundary corrosion, wherein said brass alloy comprises 62-68 % by weight of Cu, 0.02-1.00 % by weight of Pb, ⁇ 0.02 % by weight of As, 0.01-0.06 % by weight of P and/or 0.01-0.06 % by weight of Sb, and balance Zn, and the brass alloy being characterized by it comprising ⁇ 5 % of ⁇ -phase, preferably ⁇ 1 %.
  • the brass alloy according to the present invention may also comprise alloying additives such as Fe, Al, Ni, Mn, and Si in amounts as defined by the claims with the purpose of improving strength, wear resistance, and/or tensile strength.
  • alloying additives such as Fe, Al, Ni, Mn, and Si in amounts as defined by the claims with the purpose of improving strength, wear resistance, and/or tensile strength.
  • the presence of Fe, Mn, and Al in the brass alloy entails a certain increased hardness, strength, and tensile strength.
  • Si increases the strength and the resistance to wear of the brass alloy.
  • Nickel improves hardness and tensile strength without significant effect on ductility, which gives improved properties at elevated temperatures.
  • Other elements such as B, Bi, Mg, Cr, and As may also be present in the brass alloy as inevitable impurities.
  • the brass alloy comprises ⁇ 0.02 % by weight of As.
  • the brass alloy according to the present invention is produced by a method comprising the steps of
  • a brass alloy comprising ⁇ 5 % of ⁇ -phase, preferably ⁇ 1 % of ⁇ -phase, which gives improved dezincification resistance and protection against intergranular grain boundary corrosion.
  • the present invention indicates furthermore that in the presence of Al or Fe, P does not which is an unexpected technical effect (see Example 1).
  • Sb and the heat treatment at 550 °C for 2 h promotes that the ⁇ -zones are not continuous, which in turn promotes protection against intergranular grain boundary corrosion.
  • the following examples are there to illustrate a preferred embodiment and do not thereby exclude other brass alloys with both ⁇ - and ⁇ -phases falling within the scope of protection of the claims according to the present invention.
  • the example also comprises comparative experiments (with the purpose of demonstrating technical effect) between brass alloys containing different combinations of As, Sb, and/or P.
  • Test alloys 1-11 which were tested in the present application, were produced by using a base alloy having the prototype name 752 wherein the content of As, Sb, and P is as close to zero as possible.
  • the chemical composition of 752 is given in Table 1 in % by weight wherein "NBG standard value” indicates the chemical composition of the base alloy desired to be achieved while “Min” and “Max” gives the tolerances.
  • the measured composition of the base alloy is also given.
  • Table 1 Minimum, maximum, and standard values for 752 and chemical analysis of the base alloy 752, which was used for the production of the test alloys 1-11. Chemical composition % Min Max NBG std.
  • test alloys were produced in the form of ingots of 2 kg by adding As, Sb, and/or P to the base alloy in a furnace (Leybold) where the alloys were melted in a melting-pot (Morgan crucible), which had been placed in an inductance coil. The alloys were melted in the presence of air by means of ventilation above the furnace and the smelt was then poured into a mould by tipping the melting-pot together with the coil. The dimension of the mould was 40 ⁇ 40 mm (height, 300 mm).
  • Test alloys with different combinations of As, Sb, and/or P tested are given in Table 2. Alloy 3, 8, and 9 serve as comparative examples.
  • Table 2 The content of As, P, and Sb of the test alloys 1-11 indicated in % by weight. The "Analysed” contents indicate the measured % by weight while the “Planned” contents indicate the contents desired to achieve in the test alloys.
  • the chemical composition of the test alloys is presented in Table 3 wherein also inevitable impurities such as B, Bi, Mg, and Cr have been included in the table.
  • Table 3 The chemical composition of the test alloys in % by weight. Cu Zn Pb Sn Fe Al Ni Mn Si As Sb B Bi P Mg Cr min 63 0.8 .07 .45 max 64 bal.
  • test alloys 1-11 are exposed to corrosion in the form of both cast and heat-treated sample plates. Said heat treatment was made at 550 °C for 2 h, and after removal from the furnace, the samples were quickly quenched in water (with a delay of up to 5 min). As has been indicated previously, the purpose of the heat treatment is to reduce the ⁇ -phase in the test alloys.
  • the heat treatment was made at 550 °C for 2 h since comparative experiments with other temperatures and time intervals (such as 460 °C to 550 °C for 30 min-8 h) indicate that improved dezincification resistance and protection against intergranular grain boundary corrosion are obtained upon heat treatment at 550 °C for 2 h. Moreover, experiments have shown that heat treatment at 550 °C for 2 h also promotes that the ⁇ -zones are not continuous, which in turn promotes protection against IGA.
  • test alloys 1-11 were exposed to corrosion in accordance with ISO 6509 "Copper and copper alloys - brass - Determination of dezincification", in 1 % CuCl 2 solution for 24 h at 75 ⁇ 2 °C.
  • Characterizing of structures before corrosion exposure was made in the same way on etched cross-sections. Quantification was made by counting a fraction of the intersection points (mesh-intersection) of the grid which superseded 200 points; i.e., a grid is laid over the picture, then the number of points of ⁇ - and ⁇ -phase, respectively, are counted and translated into %.
  • Table 4 The amount of ⁇ -phase (%) in cast and heat-treated test alloys 1-11 (measured by using grids having intersection points (mesh-intersection), 13 ⁇ 19, with 200 ⁇ or 500 ⁇ magnification for low and high, respectively, values) As (%w) P (%w) Sb (%w) Cast Heat treated Alloy 1 - - - 13 2 Alloy 2 0.02 - - 16 4 Alloy 3 0.06 - - 13 2 Alloy 4 - 0.02 - 11 1 Alloy 5 - 0.06 - 15 2 Alloy 6 - - 0.02 10 4 Alloy 7 - - 0.06 15 2 Alloy 8 0.03 0.03 - 16 1 Alloy 9 0.03 0.03 13 1 Alloy 10 0.03 0.03 11 1 Alloy 11 0.02 0.02 0.02 15 1
  • test alloy 1-11 The results from the CuCl 2 exposure of test alloy 1-11 are presented in Table 5 where it is seen if corrosion has occurred in the ⁇ - and/or ⁇ -phase and how deep ( ⁇ m) the dezincification (AD - dezincification depth) is present.
  • Figure 2 illustrates cross-sections from test plates showing the degree of corrosion attack for representative test alloys.
  • test alloy 7, 9, 10 and 11 which all comprise Sb ⁇ 0.02 % by weight or a combination of As in an amount of ⁇ 0.02 % by weight and Sb in an amount of ⁇ 0.02 % by weight.
  • Type of corrosion Cast AD depth Type of corrosion Heat-treated AD depth As %w P %w Sb %w AD type Other attack max ( ⁇ m) mean ( ⁇ m) AD type Other attack max ( ⁇ m) mean ( ⁇ m) Alloy 1 - - - a and ⁇ 353 134 ⁇ 270 84 Alloy 2 0.02 - - ⁇ IGA 325 57 ⁇ IGA 36 10 Alloy 3 0.06 - - ⁇ IGA 282 52 ⁇ IGA 89 40 Alloy 4 - 0.02 - a and ⁇ 402 319 ⁇ 211 73 Alloy 5 - 0.06 - a and ⁇ IGA 203 100 ⁇ 328 76 Alloy 6 - - 0.02 a and ⁇ IGA 402 155 ⁇ general 106 9 Alloy 7 - - 0.06 a and ⁇ general 165 57 ⁇ general 38 0 Alloy 8 0.03 0.03 - ⁇ 178 110 ⁇ IGA 92 17

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Claims (17)

  1. Alliage de laiton ayant une résistance à la dézincification, une usinabilité et une protection contre la corrosion des joints de grain intergranulaires améliorées, comprenant
    a. 62 à 68 % en poids de Cu,
    b. 0,02 à 1,00 % en poids de Pb,
    c. ≤ 0,02 % en poids de As,
    d. 0,01 à 0,06 % en poids de P et/ou 0,01 à 0,06 % en poids de Sb,
    e. le reste étant Zn et des impuretés inévitables,
    caractérisé en ce que l'alliage de laiton comprend < 5 % de phase β, de préférence ≤ 1 % de phase β.
  2. Alliage de laiton selon la revendication 1, comprenant
    c. 0 % en poids de As,
    d. 0,02 à 0,06 % en poids de P et 0,02 à 0,06 % en poids de Sb.
  3. Alliage de laiton selon la revendication 2, comprenant
    a. 63,0 à 64,0 % en poids de Cu.
  4. Alliage de laiton selon la revendication 3, comprenant
    b. 0,80 à 1,00 % en poids de Pb.
  5. Alliage de laiton selon la revendication 1, comprenant
    c. 0 % en poids de As,
    d. 0,01 % en poids de P et 0,02 % en poids de Sb.
  6. Alliage de laiton selon la revendication 1, comprenant
    c. 0,01 % en poids de As,
    d. 0,02 % en poids de Sb.
  7. Alliage de laiton selon la revendication 1, comprenant
    c. 0,01 % en poids de As,
    d. 0,015 % en poids de P et 0,02 % en poids de Sb.
  8. Alliage de laiton ayant une résistance à la dézincification, une usinabilité et une protection contre la corrosion des joints de grain intergranulaires améliorées, comprenant
    a. 62 à 68 % en poids de Cu,
    b. 0,02 à 1,00 % en poids de Pb,
    c. ≤ 0,02 % en poids de As,
    d. 0,01 à 0,06 % en poids de P et/ou 0,01 à 0,06 % en poids de Sb,
    e. le reste étant Zn et des impuretés inévitables,
    f. 0,07 à 0,12 % en poids de Fe,
    g. 0 à 0,70 % en poids de Al,
    caractérisé en ce que l'alliage de laiton comprend < 5 % de phase β, de préférence ≤ 1 % de phase β.
  9. Alliage de laiton selon la revendication 8, comprenant
    a. 63,5 % en poids de Cu,
    b. 0,9 % en poids de Pb,
    c. 0 % en poids de As,
    d. 0,02 à 0,06 % en poids de P et 0,02 à 0,06 % en poids de Sb,
    e. 35,0 % en poids de Zn et des impuretés inévitables,
    f. 0,10 % en poids de Fe,
    g. 0,50 % en poids de Al.
  10. Alliage de laiton selon la revendication 9, comprenant
    d. 0,03 % en poids de P et 0,03 % en poids de Sb.
  11. Alliage de laiton ayant une résistance à la dézincification, une usinabilité et une protection contre la corrosion des joints de grain intergranulaires améliorées, comprenant
    a. 62 à 68 % en poids de Cu,
    b. 0,02 à 1,00 % en poids de Pb,
    c. ≤ 0,02 % en poids de As,
    d. 0,01 à 0,06 % en poids de P et/ou 0,01 à 0,06 % en poids de Sb,
    e. le reste étant Zn et des impuretés inévitables
    f. facultativement 0,07 à 0,12 % en poids de Fe,
    g. facultativement 0 à 0,70 % en poids de Al,
    h. 0 à 0,200 % en poids de Ni,
    i. 0 à 0,100 % en poids de Mn,
    j. 0 à 0,02 % en poids de Si,
    k. 0,0004 à 0,0006 % en poids de B,
    caractérisé en ce que l'alliage de laiton comprend < 5 % de phase β, de préférence ≤ 1 % de phase β.
  12. Procédé de production d'un alliage de laiton selon l'une quelconque des revendications 1 à 11, caractérisé par les étapes de
    a. ajout de Sb et/ou P à un alliage de base dans un four,
    b. la matière fondue obtenue dans l'étape α étant versée dans un moule,
    c. l'alliage de laiton coulé obtenu dans l'étape b étant traité thermiquement à 500 °C à 550 °C pendant 1 à 2 h.
  13. Procédé de production d'alliage de laiton selon la revendication 12, caractérisé en ce que l'alliage de laiton est traité thermiquement à 550 °C pendant 2 h.
  14. Utilisation de l'alliage de laiton selon l'une quelconque des revendications 1 à 11 dans des environnements qui entrent en contact avec de l'eau.
  15. Utilisation selon la revendication 14, dans laquelle lesdits environnements sont des accessoires de services de construction, de préférence sous la forme de robinets mélangeurs, de vannes et de raccords.
  16. Article qui est produit au moyen de l'alliage de laiton selon l'une quelconque des revendications 1 à 11.
  17. Utilisation de P afin de diminuer les forces de coupe de l'alliage de laiton selon l'une quelconque des revendications 8 à 11 en présence de Al ou Fe.
EP15709371.7A 2014-01-30 2015-01-30 Laiton présentant une meilleure résistance à la dézincification et une meilleure usinabilité Revoked EP3099832B1 (fr)

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SE1450094A SE1450094A1 (sv) 2014-01-30 2014-01-30 Arsenikfri mässing med förbättrad avzinkningshärdighet och skärbarhet
PCT/SE2015/050103 WO2015115989A2 (fr) 2014-01-30 2015-01-30 Laiton présentant une meilleure résistance à la dézincification et une meilleure usinabilité

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EP3099832A2 EP3099832A2 (fr) 2016-12-07
EP3099832B1 true EP3099832B1 (fr) 2018-11-14

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US (1) US20160340759A1 (fr)
EP (1) EP3099832B1 (fr)
JP (1) JP6178016B2 (fr)
KR (1) KR101802933B1 (fr)
CN (1) CN106170569A (fr)
AU (1) AU2015211433A1 (fr)
BR (1) BR112016017682A2 (fr)
CA (1) CA2937664A1 (fr)
MX (1) MX2016009812A (fr)
RU (1) RU2016133287A (fr)
SE (1) SE1450094A1 (fr)
SG (1) SG11201605577PA (fr)
WO (1) WO2015115989A2 (fr)

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JP6315868B1 (ja) * 2017-11-28 2018-04-25 日酸Ｔａｎａｋａ株式会社 ガス切断火口
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CN106170569A (zh) 2016-11-30
EP3099832A2 (fr) 2016-12-07
SE1450094A1 (sv) 2015-07-31
WO2015115989A3 (fr) 2015-09-24
US20160340759A1 (en) 2016-11-24
RU2016133287A (ru) 2018-03-05
BR112016017682A2 (pt) 2017-08-08
MX2016009812A (es) 2017-02-28
RU2016133287A3 (fr) 2018-10-15
WO2015115989A2 (fr) 2015-08-06
AU2015211433A1 (en) 2016-09-01
JP2017508073A (ja) 2017-03-23
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