WO2012113019A1 - Procédé permettant de réaliser des surfaces de travail durables - Google Patents

Procédé permettant de réaliser des surfaces de travail durables Download PDF

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Publication number
WO2012113019A1
WO2012113019A1 PCT/AU2012/000163 AU2012000163W WO2012113019A1 WO 2012113019 A1 WO2012113019 A1 WO 2012113019A1 AU 2012000163 W AU2012000163 W AU 2012000163W WO 2012113019 A1 WO2012113019 A1 WO 2012113019A1
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WO
WIPO (PCT)
Prior art keywords
gas
welding process
weld deposit
nitrogen
metal
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/AU2012/000163
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English (en)
Inventor
Mario Ciccotosto
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Individual
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Individual
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Filing date
Publication date
Priority claimed from AU2011900638A external-priority patent/AU2011900638A0/en
Application filed by Individual filed Critical Individual
Publication of WO2012113019A1 publication Critical patent/WO2012113019A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/38—Selection of media, e.g. special atmospheres for surrounding the working area
    • B23K35/383—Selection of media, e.g. special atmospheres for surrounding the working area mainly containing noble gases or nitrogen
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/32—Selection of soldering or welding materials proper with the principal constituent melting at more than 1550°C
    • B23K35/327—Selection of soldering or welding materials proper with the principal constituent melting at more than 1550°C comprising refractory compounds, e.g. carbides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/04—Welding for other purposes than joining, e.g. built-up welding
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/16—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on nitrides

Definitions

  • the present invention relates to forming durable working surfaces.
  • the invention relates to forming hardfacing surfaces by welding at the surface of metal components.
  • the invention finds its primary application in mining operations where operating conditions may be corrosive, abrasive, and erosive or a combination of these.
  • iron-based alloys have been used for components in high wear applications because, although alternative materials (such as titanium) have a longer service life, the increased service life was not sufficiently longer to make them economically viable.
  • alternative materials such as titanium
  • the commercial production of titanium and titanium alloys has increased steadily. Because of their relatively high strength to weight ratio, they initially found use in aircraft where their inherently high corrosion resistance properties were advantageous in many applications. High cost in the manufacture of titanium raw material saw its use limited principally to military applications. In recent years, however, the cost of producing alternative materials (such as high quality titanium and titanium alloy) has decreased significantly. As a consequence, these materials are finding increased use in the mining and mineral processing industries, where equipment manufacturers and designers are specifying their use because of their chemical and mechanical properties.
  • Titanium & Titanium alloys for use in the said industries include pipes, pipe fittings, valve components, agitation components and pressure vessels to name some. In the presence of abrasive particles and flowing conditions, these components can sustain life limiting damage in the form of accelerated material loss. Common failure or degradation mechanisms encountered include high angle and low angle abrasion, adhesive wear, erosion, erosion - corrosion and cavitation. This is primarily because of the relatively low hardness and poor tribological properties of titanium and titanium alloys.
  • Titanium & Titanium alloys A number of different surface heat treatment technologies are used on Titanium & Titanium alloys to improve wear and tribological properties. Included in this group are the use of lasers and plasma to alter the microstructure of the surface - layers (without altering the chemistry) by rapid melting and solidification.
  • Titanium & Titanium alloys can be applied to alter the surface properties. Included here are processes such as plating (eg copper, hard chrome and electroless nickel), physical vapour deposition (eg sputtering of TiN onto drill bits) and thermally sprayed coatings (eg plasma spraying and high velocity oxyfuel).
  • plating eg copper, hard chrome and electroless nickel
  • physical vapour deposition eg sputtering of TiN onto drill bits
  • thermally sprayed coatings eg plasma spraying and high velocity oxyfuel.
  • Titanium & Titanium alloys are very chemically active and react readily with interstitial elements. As such, these materials can be hardened by the diffusion of oxygen, carbon, nitrogen and boron at elevated temperatures (almost always in the solid state), where they form hard phases within the surface layers.
  • the treated substrate will possess an effective or transformed layer that is very thin. In many cases, this will be ⁇ 200pm and in almost all cases, it will be ⁇ 1000pm. In practical terms, components employed in the mineral processing and mining industries, that are treated using any of these techniques, would not return any significant benefit in service life.
  • the object of the invention is to provide alternative methods for preparing durable working surfaces on metal components.
  • metal component as used throughout this specification is taken to mean a product formed of a transition metal or a transition metal alloy.
  • welding deposit as used throughout this specification is taken to mean that volume of molten metal that has solidified on the surface of a component, or previous deposit, as a result of a welding process.
  • a method for producing a durable working surface on a metal component by forming a weld deposit comprising metal nitrides.
  • the method involves controlling the content of nitrogen in a shielding gas to cause nitrogen gas to react with metal in a weld pool so that, upon solidification, the weld deposit comprises an amount of metal nitrides.
  • the metal nitrides comprise 20 to 90 vol% of the weld deposit. This is considered to be a useful range of metal nitride for providing the principal purpose of increased wear resistance under various aggressive operating conditions. It is believed that below 20 vol% metal nitrides, the increase in bulk hardness achieved may not in some cases be sufficient to provide adequate wear resistance.
  • Welding metals that have a high affinity for oxygen, as is the case with many of the transition metals traditionally involves using a shielding gas.
  • the shielding gas comprises predominantly, or wholly, of argon.
  • the purpose of the shielding gas is to prevent contamination of the weld deposit caused by reaction with the general atmosphere.
  • the formation of unwanted phases or constituents in the weld deposit, such as metal oxides, are deleterious to the weld integrity. Accordingly, the shielding gas used is protective in nature and does not react with the weld metal. By displacing atmospheric air from the weld pool during melting and solidification, reaction with the general atmosphere is prevented and as a result, contamination of the weld is avoided.
  • the welding operation is conducted not with the typical shielding gas, but with a shielding gas containing nitrogen.
  • nitrogen is absorbed into the weld pool.
  • metal nitride is formed.
  • the volume and composition of the metal nitride produced is dependent largely upon the amount of nitrogen absorbed during the welding operation.
  • the welding operation can be influenced by a number of operating variables. These include voltage, current, wire consumable diameter, welding travel speed, shielding gas composition, shielding gas flow rate and the consumable grade.
  • suitable weld procedure specifications must be established for the materials being welded.
  • the shielding gas substantially will comprise nitrogen.
  • the shielding gas may comprise at least 50 vol% nitrogen, preferably at least 70 vol%, more preferably at least 80 vol% and even more preferably at least 90 vol%.
  • the shielding gas may comprise nitrogen and argon or nitrogen and helium or nitrogen, argon and helium.
  • the relative make up of the balance of the shielding gas is not critical however, where additional arc energy is beneficial to the welding operation, helium may be used in preference to argon.
  • the shielding gas may totally comprise nitrogen.
  • a hard facing weld deposit comprising a transition metal or a transition metal alloy produced by a welding method according to the first aspect wherein the weld deposit comprises metal nitride in the range of 20 to 90 vol%.
  • the weld deposit may have a thickness on a work piece in the range of 0.1 to 30mm.
  • the weld deposit may comprise multiple layers of weld.
  • the thickness may be 0.1 to 5mm for a single layer, and greater than 5mm and more preferably greater than 10mm, for multiple layers.
  • the weld deposit may possess a bulk hardness in the range of 400 to 1000 HV. This range may be higher or lower depending on the transition metal consumable used and welding parameters adopted.
  • the method uses the gas metal arc welding (GMAW) process incorporating transition metal or transition metal alloy wire consumable. It is preferable, though not necessary, to conduct the process using a constant voltage, direct current power supply. It should be noted that the invention as described can also be applied to other forms of fusion welding.
  • the commonly used process of gas tungsten arc welding (GTAW) is an appropriate welding technique for producing weld deposits using transition metal and transition metal alloy consumables.
  • GTAW gas tungsten arc welding
  • the shielding gas used must contain an appropriate quantity of nitrogen such that the formation of metal nitride occurs.
  • the welding parameters must be appropriately developed for the consumable such that the transition metal nitride forms in sufficient quantities and with a distribution and morphology that imparts desirable metallurgical qualities. Acicular and dendritic morphologies are considered to be acceptable, whereas metal nitride that is present as a grain boundary film would be considered to be a deleterious morphology. A uniform distribution of the acicular and dendritic nitrides is preferred.
  • the method according to the first aspect can be applied to both manual and automatic GTAW.
  • PTAW plasma transferred arc welding
  • any welding operation that utilises a heat source to melt a metallic consumable and fuse it to a metallic substrate is suitable for using this invention.
  • other suitable processes include solid state laser welding, gaseous laser welding, fibre optic laser welding and hybrid-laser welding.
  • Figure 1 is a schematic cross-section of a typical GMAW head assembly in operation.
  • Figure 2 is a schematic cross-section of a typical GTAW head assembly in operation.
  • Figure 3 is a schematic cross-sectional sketch of a typical PTAW head assembly in operation.
  • Figure 4 is a photograph showing the microstructure of weld deposit produced according to the first aspect of the invention with a GTAW method containing -30 vol% titanium nitride.
  • Figure 5 is a photograph showing the microstructure of weld deposit produced according to the first aspect of the invention with a GTAW method containing -60 vol% titanium nitride.
  • Figure 6 is a photograph showing the microstructure of weld deposit produced according to the first aspect of the invention with a GTAW method containing ⁇ 80 vol% titanium nitride. DESCRIPTION OF PREFERRED EMBODIMENTS
  • FIG. 1 there is shown a schematic drawing of a cross-section of a typical GMAW head in operation, comprising of a wire consumable 10, contact tube 12, gas diffuser 14, and nozzle 16. Shielding gas 18 is supplied to the head and passes through the diffuser 14. Not shown is the wire feed unit, power supply unit and the gas supply.
  • FIG. 2 shows a schematic cross-section of a typical GTAW head. Not shown is the power source, gas supply and commonly used cooling system. Found within the head is a non-consumable tungsten electrode 10, a supporting collet 12, a collet body 14, and a gas diffuser 16. A high frequency generator (or similar device) is used to initiate an arc between the work piece and tungsten electrode 10. As the filler consumable 20 is manually or automatically fed into the path of the arc, it melts forming a weld pool. Nitrogen-containing shielding gas 18 is supplied to blanket the molten weld pool and heat affected zones, until such time as the weld solidifies. Prior to solidifying, the weld pool absorbs a quantity of the introduced nitrogen which reacts with the metal to produce a deposit containing an amount of titanium nitride.
  • FIG. 3 is a schematic cross-section of a typical PTAW head. It shows a central tungsten electrode 10 located within a copper plasma nozzle 14, which contains the primary ionising or plasma gas 12. Powdered consumable 16 is introduced to the tip of the electrode 10 via a second nozzle 18. The consumable is usually delivered with a carrier gas to improve the flow and increase the feed rate. Located at the tip of the nozzle is a small, constricting orifice. A pilot arc is initiated between the tungsten electrode 10 and copper plasma gas nozzle 14, and this arc is then transferred to the work piece. Consumable powder 16 is introduced into the arc stream in the presence of the plasma gas 12.
  • the energy delivered to the work piece surface is very concentrated, producing high quality weld deposits.
  • a secondary gas is used for shielding of the molten weld pool.
  • the shielding gas 20 contains a substantial amount of nitrogen so that titanium nitride can form in the weld deposit upon solidification.
  • nitrogen can also be added to the plasma gas 12. The whole assembly is contained within an outer housing 22.
  • Test 1 ( Figure 4) produced a weld deposit having a TiN content of ⁇ 30 vol%.
  • the TiN content is attributed with raising the hardness of the weld deposit to ⁇ 430 HV5. This is 240 HV greater than the parent titanium substrate.
  • the high hardness and depth of the weld deposit make the titanium alloy more suited to applications in which higher wear resistance is important.
  • Test 2 ( Figure 5) produced a weld deposit having a TiN content of -60 vol% and a hardness around 700 HV5. This was more than 500 HV higher than the underlying plate hardness and 270 HV harder than Test 1.
  • Test 3 ( Figure 6) produced a weld deposit having a TiN content around 80 vol
  • Hard, nitride containing weld deposits can also be produced using other transition metals and their alloys using similar principles. These include, but are not limited to, tantalum, zirconium, tungsten, niobium, chromium, molybdenum, vanadium and their alloys.
  • shielding gas is used to describe shielding gas, and / or carrier gas, and / or plasma gas as appropriate for the welding process being described or discussed.
  • Statements regarding welding practices being "known” or “common” or to similar effect are not an admission that the practices form part of the common general knowledge of a skilled person in Australia or in any other jurisdiction.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Arc Welding In General (AREA)

Abstract

L'invention concerne des procédés décrivant la réalisation de dépôts de soudage durs en utilisant un certain nombre de différentes techniques de soudage. Les dépôts de soudage produits contiennent une quantité de métal nitrure qui a pour effet d'accroître la dureté. Les produits consommables de soudage et les substrats métalliques pour lesquels ces procédés conviennent comprennent, mais sans s'y limiter, le titane, le tantale, le zirconium, le hafnium, le molybdène, le vanadium, le niobium, le tungstène, le fer, le nickel et leurs alliages.
PCT/AU2012/000163 2011-02-24 2012-02-20 Procédé permettant de réaliser des surfaces de travail durables Ceased WO2012113019A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AU2011900638 2011-02-24
AU2011900638A AU2011900638A0 (en) 2011-02-24 Method of Forming Durable Working Surfaces

Publications (1)

Publication Number Publication Date
WO2012113019A1 true WO2012113019A1 (fr) 2012-08-30

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PCT/AU2012/000163 Ceased WO2012113019A1 (fr) 2011-02-24 2012-02-20 Procédé permettant de réaliser des surfaces de travail durables

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2557180C1 (ru) * 2014-03-19 2015-07-20 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Национальный исследовательский Томский политехнический университет" СПОСОБ ПЛАЗМЕННОЙ НАПЛАВКИ ПОРОШКОВ СИСТЕМЫ Fe-Cr-V-Mo-C
WO2017147096A1 (fr) * 2016-02-22 2017-08-31 Bwxt Nuclear Operations Group, Inc. Commande de précipitation de carbure/nitrure métallique dans un soudage par fusion
CN110670068A (zh) * 2019-11-27 2020-01-10 江苏科技大学 一种高耐磨耐腐蚀等离子熔覆金属涂层及其制备方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3111434A (en) * 1960-08-01 1963-11-19 Kobe Steel Ltd Surface hardening of metal body consisting of or containing titanium or zirconium
GB2328221A (en) * 1997-08-15 1999-02-17 Univ Brunel Surface treatment of titanium alloys
JP2006095589A (ja) * 2004-09-30 2006-04-13 Teigu:Kk チタン材料の表面硬化方法
WO2007124310A2 (fr) * 2006-04-20 2007-11-01 Materials & Electrochemical Research Corp. Procédé d'utilisation de plasma thermique pour produire une couche superficielle composite fonctionnellement calibrée sur des métaux

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3111434A (en) * 1960-08-01 1963-11-19 Kobe Steel Ltd Surface hardening of metal body consisting of or containing titanium or zirconium
GB2328221A (en) * 1997-08-15 1999-02-17 Univ Brunel Surface treatment of titanium alloys
JP2006095589A (ja) * 2004-09-30 2006-04-13 Teigu:Kk チタン材料の表面硬化方法
WO2007124310A2 (fr) * 2006-04-20 2007-11-01 Materials & Electrochemical Research Corp. Procédé d'utilisation de plasma thermique pour produire une couche superficielle composite fonctionnellement calibrée sur des métaux

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
DATABASE WPI Derwent World Patents Index; AN 2006-259523 *

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2557180C1 (ru) * 2014-03-19 2015-07-20 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Национальный исследовательский Томский политехнический университет" СПОСОБ ПЛАЗМЕННОЙ НАПЛАВКИ ПОРОШКОВ СИСТЕМЫ Fe-Cr-V-Mo-C
WO2017147096A1 (fr) * 2016-02-22 2017-08-31 Bwxt Nuclear Operations Group, Inc. Commande de précipitation de carbure/nitrure métallique dans un soudage par fusion
US10543570B2 (en) 2016-02-22 2020-01-28 Bwxt Nuclear Operations Group, Inc. Metal carbide/nitride precipitation control in fusion welding
US11413710B2 (en) 2016-02-22 2022-08-16 Bwxt Nuclear Operations Group, Inc. Metal carbide/nitride precipitation control in fusion welding
US12263542B2 (en) 2016-02-22 2025-04-01 Bwxt Nuclear Operations Group, Inc. Metal carbide/nitride precipitation control in fusion welding
CN110670068A (zh) * 2019-11-27 2020-01-10 江苏科技大学 一种高耐磨耐腐蚀等离子熔覆金属涂层及其制备方法

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