US20080206089A1 - Ni-Cr-Fe Alloy For High-Temperature Use - Google Patents

Ni-Cr-Fe Alloy For High-Temperature Use Download PDF

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Publication number
US20080206089A1
US20080206089A1 US11/994,372 US99437206A US2008206089A1 US 20080206089 A1 US20080206089 A1 US 20080206089A1 US 99437206 A US99437206 A US 99437206A US 2008206089 A1 US2008206089 A1 US 2008206089A1
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alloy
level
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alloys
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Rikard Norling
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Sandvik Intellectual Property AB
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • H—ELECTRICITY
    • H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
    • H05B—ELECTRIC HEATING; ELECTRIC LIGHT SOURCES NOT OTHERWISE PROVIDED FOR; CIRCUIT ARRANGEMENTS FOR ELECTRIC LIGHT SOURCES, IN GENERAL
    • H05B3/00—Ohmic-resistance heating
    • H05B3/10—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor
    • H05B3/12—Heating elements characterised by the composition or nature of the materials or by the arrangement of the conductor characterised by the composition or nature of the conductive material
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W

Definitions

  • the present invention relates to a Ni—Cr—Fe alloy for use at high temperatures.
  • Austenitic alloys based on the Ni—Cr and the Ni—Cr—Fe system with chromium contents of up to 30% by weight and silicon contents up to 3% by weight have been used for many years for high-temperature uses, up to operating temperatures of 1,100° C. These alloys often contain also additions of small quantities of rare earth metals.
  • a number of such alloys with different nickel levels, intended to be used as electrical resistance materials for heating in, among other applications, industrial furnaces and household appliances have been defined as standards in ASTM B 344-01 and in DIN 17 470 (together with DIN 17 742). These standards are not fully in agreement with each other, as can be seen in Table 1.
  • Table 1 also specifies the nominal composition of a non-standard alloy, as specified by U.S. Pat. No. 2,858,208. This alloy is, as far as is known, no longer commercially available, but it has received a certain amount of previous use for the same applications.
  • Ni—Cr—(Fe) resistive materials as specified by the DIN and ASTM standards, and that of an alloy as specified by U.S. Pat. No. 2,858,208.
  • electrical resistive materials have, in addition to a high oxidation stability, a relatively high electrical resistivity such that it is possible to obtain the desired power development within an electrical heating element with given limitations in dimensions and weight. It is generally the case that if an electrical heat element with a certain nominal power is manufactured with the same cross-sectional area as the conductor, an alloy with a higher resistivity gives rise to a shorter conductor and thus a saving in weight, which leads directly to a saving in costs.
  • the change in resistivity at elevated temperature, C t is given by the ratio between the electrical resistance at the working temperature and that at room temperature for an electrical resistive material. This parameter is an important factor in obtaining an even distribution of temperature along the electrical resistive element, particularly when the total service time increases. The lower the value of C t , the more even will be the distribution of temperature, and this will normally result in a longer life-time for the element, since the risk of local overheating is reduced. It is generally the case that C t decreases with increasing Ni content, but the levels of Cr, Fe and Si are also significant. The C t -value for resistive material with a Ni content of over 40% depends also on the rate at which the alloy cooled following the most recent heating to red-hot.
  • Table 2 gives typical values for the resistivity at room temperature and of C t at 1,000° C. for alloys with compositions as specified by ASTM B 344-01 and by DIN 17 470, together with an alloy as specified by U.S. Pat. No. 2,858,208. All of the alloys tested were tested in the form of wire that had been heated to red-hot and then allowed to cool freely in air after the annealing.
  • the values in Table 2 are based on comparative measurements taken on one and the same measurement occasion by the applicant, and are not taken directly from the published standards. These standards give recommended values only, or they prescribe intervals that are so large that the values given cannot be directly compared.
  • the C t -value in this case has been determined as specified by ASTM B70-90 with one modification: the resistivity of the test material before the test was used as reference value for calculating the C t -value, and not the resistivity after the test had been carried out.
  • the C t -value is particularly significant for the life-time of the cover at high operating temperatures of tube elements with metal cover, which consist of an electrical heating coil embedded in an electrically insulating MgO powder placed inside of the cover. This is a result of the fact that the insulating properties of MgO depend very heavily on the temperature, and thus zones of elevated temperature have a tendency to cause leakage currents or even short-circuits between the heating coil and the metal cover.
  • a typical application for tube elements with a metal cover with a high operating temperature of the cover is that of grill element in a domestic oven. It is well-known that elements with heating coils made from alloys of the type NiCr 80 20 achieve a more even distribution of temperature along the element and a longer life-time than equivalent elements with the heating coil made of alloys of the type NiCr 60 15. The more even distribution of temperature of the first-named type of element also leads to a more even distribution of heat in the domestic oven, something that is normally desired.
  • Alloys based on the Fe—Cr—Al system are also used as tube elements in general, and in particular as water-heating tube elements. These alloys, however, are not suitable for elements that operate under such conditions of load that the cover glows red, since it is well-known that the presence of Al in the alloys in these cases leads over time to poor insulating ability of the MgO powder.
  • Nb, Mo and W additives for some nickel-based alloys with the aim of improving the mechanical properties at high temperatures.
  • the high cost of these alloy elements means that this procedure is not desirable for application in which the cost is a significant factor.
  • the addition of Nb also leads to a lower hot workability of the alloy, which results in a reduction in the productivity during hot-rolling, and this introduces an increase in production costs.
  • a level of C that is higher than 0.1% by weight is found in certain nickel-based alloys for high-temperature use. These alloys are known as “cast alloys” and they are not suitable for working using normal methods such as rolling and extrusion, which are used, among other applications, to form electrical resistive material.
  • the high content of carbon makes these alloys also unsuitable for use as electrical resistive material for heating due to, among other factors, their limited oxidation stability.
  • Alloys with a Cr content greater than 25% by weight generally have poor workability properties, which results in high production costs. This limits the use of such alloys, for example of the type NiCr 70 30, to applications in which the cost is less significant.
  • the present invention offers compositions of an alloy of Ni—Cr—Fe that combines a relatively low cost of production, if possible as low as that of NiCr 60 15, with the following properties: good oxidative stability, a relatively high electrical resistivity, and a small change in resistivity with increasing temperature such as, for example, that of NiCr 80 20.
  • Important factors for achieving a low cost of production are the good hot workability of the compositions, and the low overall content of expensive alloy elements such as nickel and cobalt.
  • the present invention thus relates to an alloy for use at high temperature, characterised in that the alloy principally consists of Ni, Cr and Fe and in that the alloy has a principal composition such that the levels of the elements Cr, Fe, Si, C and Nb lie within the following intervals of percentage by weight:
  • the alloy according to the present invention should contain at least 57% Ni, preferably at least 60%.
  • the alloy can furthermore contain Al, Ca, Cu, Hf, Mg, Mn, Mo, N, Ta, Ti, V, W, Y, Zr and rare earth metals up to a total of 7% and impurities up to a maximum of 1%.
  • Co can replace Ni by up to 5%.
  • FIG. 1 shows a region of advantageous and particularly advantageous compositions of the alloy according to the invention in comparison with existing alloys, in the form of a phase diagram
  • FIG. 2 shows a region of advantageous and particularly advantageous compositions of the alloy according to the invention with a level of Si of 2%, in the form of a phase diagram, and
  • FIG. 3 shows an alternative region of advantageous and particularly advantageous compositions of the alloy according to the invention with a level of Si of 2%, in the form of a phase diagram.
  • an alloy according to the invention is characterised in that its C t -value at 1,000° C. is 1.10 or lower.
  • the C t -value can be measured as specified by, for example, the standard ASTM B70-90.
  • Table 5 gives a qualitative evaluation of raw materials cost, hot workability, oxidative stability and tube element life-time of the test smelts.
  • a qualitative evaluation of the resistivity and C t -value of the alloys has also been included in order to facilitate comparison.
  • the evaluation of raw materials cost is based on the level of Ni in the alloys and the evaluation of hot workability is based on the results of the hot-rolling.
  • the oxidative stability has been evaluated by heating test wires with a constant power that is produced by an electric current that is led through them, whereby the test wires have been cyclically exposed with periods of two minutes on and two minutes off. The times taken for the wires to burn through have been recorded and mutually compared.
  • the life-time of the tube elements has been evaluated by testing tube elements with a metal cover, which elements have been manufactured by conventional methods with a resistive wire from each test smelt.
  • the testing has been carried out such that each tube element has been subject to cyclic loading with a constant electrical power in periods of 60 minutes on and 20 minutes off.
  • the times taken for the tube elements to cease to function have been recorded and mutually compared.
  • FIG. 1 shows an overview of the region in which advantageous and particularly advantageous compositions of the alloy according to the invention can be found.
  • the compositions of existing NiCr(Fe) resistive alloys according to Table 1 have been marked for comparison.
  • the drawing is only an illustration and it does not take into consideration small deviations that depend on the presence of other alloy elements than Ni, Co, Fe and Cr.
  • An alloy according to the invention contains at least 1% Si, preferably at least 1.5% Si. Addition of Si raises the oxidative resistance and the resistivity, and it lowers the C t -value.
  • the alloy contains also up to 5% Co as replacement for Ni, and up to 2% Mn.
  • the alloy can also contain in addition to this Al at a level of up to 0.4% and rare earth metals (lanthanides, i.e. elements from La to Lu), Y, Ca and Mg up to a total level of 0.3%. It can furthermore contain elements that form nitrides and carbides such as Ti, Zr, Hf, Nb, Ta, and V up to a total level of 0.4%, values of these substances that are too high, however, can lead to the alloy becoming difficult to manufacture.
  • the level of C is lower than 0.1% and the level of N does not exceed 0.2%.
  • the total level of Cu, Mo and W does not exceed 1%.
  • Other substances that constitute impurities in the present alloy and that are derived from raw materials and the manufacturing process can be present in levels up to 1%.
  • FIG. 2 shows in detail the region of these compositions for a level of Si of 2%. The way in which the region is changed with an increasing or decreasing level of Si is indicated in the drawing.
  • the alloy contain also up to 5% Co as replacement for Ni, and up to 2% Mn.
  • the alloy can also contain in addition to this Al at a level of up to 0.4% and rare earth metals (lanthanides, i.e. elements from La to Lu), Y, Ca and Mg up to a total level of 0.3%. It can furthermore contain elements that form nitrides and carbides such as Ti, Zr, Hf, Nb, Ta, and V up to a total level of 0.4%.
  • the level of C is lower than 0.1% and the level of N does not exceed 0.2%.
  • the total level of Cu, Mo and W does not exceed 1%.
  • Other substances that constitute impurities in the present alloy and that are derived from raw materials and the manufacturing process can be present in levels up to 1%.
  • FIG. 3 shows in detail the region of these compositions for a level of Si of 2%. The way in which the region is changed with an increasing or decreasing level of Si is indicated in the drawing.
  • the alloy contains (levels are given in percentages by weight):
  • composition has been smelted using an industrial method and at full scale, it has been hot-rolled and cold-drawn to wire as specified by standard procedures and it has thus obtained the following advantageous properties:
  • the life time of the alloy according to the example when the element is an uninsulated freely radiating heating element in an industrial oven has been investigated.
  • the furnace temperature was 900° C. and the element was fed with a constant power during periods of 90 seconds and no power during 30 seconds.
  • the resulting life time was approximately the same as the life time of the alloy N i C r 70 30, 25% lower than for N i C r 80 20 and 65% lower than for N i C r 60 15.
  • Nb is low. This is illustrated by the following. A smelt was prepared using the same method of manufacture and with an identical composition as in the example above, except for the addition of 0.2 percent by weight of Nb.
  • Nb resulted in the oxidative life-time being shortened by over 40% and the hot workability becoming worse, to a level corresponding to that of NiCr 70 30.
  • the resistivity and the C t -value were unchanged.
  • the life time of the heating element was shortened with almost 50%.
  • a certain low level of Nb can, however, be accepted for certain applications even if certain properties are poorer, due to the fact that the manufacturing cost becomes lower than that of known material with corresponding properties.
  • the effect of an addition of Ta are expected to be the same as those of the addition of Nb in the present alloy.
  • the level of Ta should, for this reason, also be limited up to a value of 0.2 percent by weight.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Resistance Heating (AREA)
  • Conductive Materials (AREA)
  • Soft Magnetic Materials (AREA)
US11/994,372 2005-07-01 2006-06-16 Ni-Cr-Fe Alloy For High-Temperature Use Abandoned US20080206089A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
SE0501536A SE529003E (sv) 2005-07-01 2005-07-01 Ni-Cr-Fe-legering för högtemperaturanvändning
SE0501536-7 2005-07-01
PCT/SE2006/050201 WO2007004973A1 (en) 2005-07-01 2006-06-16 Ni-cr-fe alloy for high-temperature use.

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PCT/SE2006/050201 A-371-Of-International WO2007004973A1 (en) 2005-07-01 2006-06-16 Ni-cr-fe alloy for high-temperature use.

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US13/157,550 Division US8926769B2 (en) 2005-07-01 2011-06-10 Ni—Cr—Fe alloy for high-temperature use

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US13/157,550 Expired - Fee Related US8926769B2 (en) 2005-07-01 2011-06-10 Ni—Cr—Fe alloy for high-temperature use

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EP (1) EP1899489B1 (ja)
JP (1) JP5300473B2 (ja)
KR (1) KR101322091B1 (ja)
CN (1) CN101213315B (ja)
DK (1) DK1899489T3 (ja)
ES (1) ES2447022T3 (ja)
PL (1) PL1899489T3 (ja)
SE (1) SE529003E (ja)
WO (1) WO2007004973A1 (ja)

Cited By (2)

* Cited by examiner, † Cited by third party
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EP2647732A1 (en) * 2010-11-30 2013-10-09 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Precipitation-strengthened ni-based heat-resistant alloy and method for producing the same
US8593045B2 (en) 2010-06-02 2013-11-26 Ngk Spark Plug Co., Ltd. Spark plug

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CN102732751B (zh) * 2012-06-18 2014-06-04 江苏新华合金电器有限公司 核电站蒸汽发生器用抗振合金材料及其制备方法
CN103938032B (zh) * 2014-05-12 2016-05-11 盐城市鑫洋电热材料有限公司 一种提高镍铬系电热合金使用寿命的方法
CN104046881A (zh) * 2014-07-01 2014-09-17 张家港市佳晟机械有限公司 一种镍铬电热合金
US9528171B2 (en) 2014-09-16 2016-12-27 Caterpillar Inc. Alloy for seal ring, seal ring, and method of making seal ring for seal assembly of machine
CN106282729B (zh) * 2016-08-31 2018-01-16 彭书成 一种超级合金及其制备方法
TWI641001B (zh) * 2018-01-22 2018-11-11 國立屏東科技大學 薄膜電阻合金
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CN110129732B (zh) * 2019-05-23 2020-08-11 北京理工大学 一种高电阻率高熵合金薄膜及其制备方法
KR102239330B1 (ko) 2019-06-12 2021-04-12 엘지전자 주식회사 제어된 산화막을 가지는 면상 발열체 및 그 제조방법
KR102396584B1 (ko) * 2019-06-12 2022-05-10 엘지전자 주식회사 면상 발열체 및 그 제조방법
CN112522545B (zh) * 2020-11-27 2021-12-14 成都先进金属材料产业技术研究院股份有限公司 镍铬高电阻电热合金

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US4400211A (en) * 1981-06-10 1983-08-23 Sumitomo Metal Industries, Ltd. Alloy for making high strength deep well casing and tubing having improved resistance to stress-corrosion cracking
US4994118A (en) * 1988-07-28 1991-02-19 Thyssen Stahl Ag Process for the production of hot rolled steel or heavy plates
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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8593045B2 (en) 2010-06-02 2013-11-26 Ngk Spark Plug Co., Ltd. Spark plug
EP2647732A1 (en) * 2010-11-30 2013-10-09 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Precipitation-strengthened ni-based heat-resistant alloy and method for producing the same
EP2647732A4 (en) * 2010-11-30 2014-12-03 Kobe Steel Ltd Precipitation-hardened, nickel-base-based, heat-resistant alloy and process for producing the same
US9238857B2 (en) 2010-11-30 2016-01-19 Kobe Steel, Ltd. Precipitation-strengthened Ni-based heat-resistant alloy and method for producing the same

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CN101213315B (zh) 2012-06-27
SE529003C2 (sv) 2007-04-03
DK1899489T3 (en) 2014-02-17
WO2007004973A1 (en) 2007-01-11
EP1899489A1 (en) 2008-03-19
CN101213315A (zh) 2008-07-02
KR101322091B1 (ko) 2013-10-25
US20110259875A1 (en) 2011-10-27
PL1899489T3 (pl) 2014-05-30
SE529003E (sv) 2011-10-11
EP1899489B1 (en) 2013-12-18
SE0501536L (sv) 2007-01-02
JP5300473B2 (ja) 2013-09-25
JP2009500521A (ja) 2009-01-08
KR20080027866A (ko) 2008-03-28
US8926769B2 (en) 2015-01-06
EP1899489A4 (en) 2010-08-18
ES2447022T3 (es) 2014-03-11

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