EP2616561B1 - Optimisation de l'usinabilite d'aciers martensitiques inoxydables - Google Patents

Optimisation de l'usinabilite d'aciers martensitiques inoxydables Download PDF

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Publication number
EP2616561B1
EP2616561B1 EP11773051.5A EP11773051A EP2616561B1 EP 2616561 B1 EP2616561 B1 EP 2616561B1 EP 11773051 A EP11773051 A EP 11773051A EP 2616561 B1 EP2616561 B1 EP 2616561B1
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EP
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Prior art keywords
temperature
steel
fabricating
cooling
martensitic stainless
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EP11773051.5A
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German (de)
English (en)
French (fr)
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EP2616561A1 (fr
Inventor
Jean-François Laurent CHABOT
Laurent Ferrer
Pascal Charles Emile Thoison
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Safran Aircraft Engines SAS
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SNECMA SAS
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the percentages of composition are percentages by weight unless otherwise specified.
  • a stainless martensitic steel is a steel with a chromium content greater than 10.5%, and whose structure is essentially martensitic (ie the amount of alphagenic elements is sufficiently high compared to that of the elements Gammagens - see explanations below).
  • This half-product is then pre-cut into sub-elements which are shaped (for example by forging or rolling) in order to give them a shape approximating their final shape.
  • Each sub-element thus becomes a part with overthicknesses (called part in the rough state) with respect to the final dimensional dimensions of use.
  • the objective of the phase (A) is to homogenize the microstructure within the part, and to re-dissolve soluble particles at this temperature by recrystallization.
  • Phase (B) has as its primary objective a maximum transformation of austenite to martensite within the steel part.
  • transformations of the martensitic microstructure do not occur simultaneously at any point in the room, but gradually from its surface to its core.
  • the change in crystallographic volume that accompanies these transformations therefore generates internal stresses and, at the end of quenching (because of the low temperatures then reached), limits the relaxations of these stresses.
  • the second objective is to minimize the risk of quenching taps, that is to say the appearance of cracks on the surface of the workpiece by the release of residual stresses in the steel in a weak metallurgical martensitic state.
  • phase (C) a treatment of income
  • T max is substantially equal to the nominal temperature M F end of martensitic transformation of the steel, ie from 150 to 200 ° C for a martensitic stainless steel.
  • T min is 20 to 28 ° C depending on the chemical composition. It then remains in the steel a residual austenite rate that could not be transformed.
  • Phase (C) - first treatment of income - of this quality heat treatment aims on the one hand a transformation of fresh martensite into martensite revenue (more stable and more tenacious) and on the other hand a destabilization of the residual austenite from previous phases.
  • phase (D) - cooling of the first income - of this quality heat treatment aims to transform the residual austenite into martensite.
  • the hottest part of the room must also be cooled down to a temperature within the temperature range [T max ; T min ].
  • phase (E) - second treatment of income - of this heat treatment of quality aims at the transformation of the new fresh martensite into martensite revenue (more stable and tenacious) aiming to reach the best compromise in the mechanical properties of the steel.
  • phase (F) - cooling of the second income - of this quality heat treatment brings the raw room to room temperature.
  • the documents FR 2 920 784 and FR 2 893 954 disclose the manufacture of a martensitic stainless steel by austenitization followed by tempering and two incomes.
  • the present invention aims to provide a manufacturing method that improves the machinability of these steels.
  • thermomechanical treatments such as forging, rolling
  • This blank is then intended to be machined to give it its final shape after performing the heat treatment quality.
  • the blank in this steel is heated to a temperature above the austenization temperature T AUS , and the workpiece is maintained at this temperature until the entire workpiece is at a temperature of temperature above the austenization temperature T AUS (austenization of steel).
  • the steel is then quenched sufficiently fast so that the austenite does not turn into a ferrito-pearlitic structure (see explanations and figure 3 below).
  • the majority of the volume of the steel part is likely to turn into martensite, since the austenite can only be transformed into martensite if it has not previously been transformed into a ferrito-pearlitic structure.
  • the austenization of the steel and then its quenching corresponds to treatment 1 on the figure 1 .
  • the steel solidifies gradually during its cooling. This solidification takes place by growth of dendrites 10, as illustrated in FIG. figure 2 .
  • the dendrites 10, corresponding to the first solidified grains are by definition richer in alphagenes elements while the interdendritic regions 20 are richer in elements, gamma (application of the rule known segments on the phase diagram).
  • An alphagene element is an element that favors a ferritic type structure (structures that are more stable at low temperature: bainite, ferrite-pearlite, martensite).
  • a gammagenic element is an element that favors an austenitic structure (stable structure at high temperature: austenite). There is therefore segregation between dendrites 10 and interdendritic regions 20.
  • the figure 3 is a known temperature (T) - time (t) diagram for a steel according to the invention when it is cooled from a temperature above the austenitic temperature T AUS .
  • Curves D and F mark the beginning and the end of the austenite transformation (region A) in a ferrito-pearlitic structure (FP region). This transformation takes place, partially or fully, when the cooling curve C that following the ingot passes respectively in the region between the D and F curves or in the FP region. It does not take place when the cooling curve C is entirely in the region A, as illustrated in FIG. figure 3 .
  • curves D, F, M S , and M F in solid lines are valid for structures richer in alphagenic elements (that is to say in the dendrites of steel), whereas the same curves in lines dotted d ', F', M S , and M F are valid for structures richer in gammagene elements (that is to say in the interdendritic spaces of steel).
  • austenite transformation curves in the ferrito-pearlitic structure in the case of interdendritic spaces are shifted to the right with respect to the austenite transformation curves into a ferrito-pearlitic structure in the dendrites (curves D and F). It takes more time at a given temperature to transform the austenite into a ferritic-pearlitic structure in the case of interdendritic spaces than in the case of dendrites.
  • the cooling of the steel during quenching after austenisation follows curve C of the figure 3 .
  • the steel goes below the temperature of martensitic transformation end in cooling M F interdendritic spaces. Due to the cooling process, the skin temperature of the room is lower than the temperature in the heart of the room, which is its hottest part.
  • This heating is effected for example by placing the room in an environment (preheated oven or heating chamber) where there is a temperature at least equal to the maximum temperature T max .
  • a first income of the steel is then made by continuing to heat it up to a temperature T R , which is lower than the austenitic temperature T AUS .
  • This income makes it possible to stabilize the fresh martensitic crystallographic phase by, for example, precipitating carbides within the martensite and thus imparting more resilience to the martensite of the steel.
  • This first income treatment corresponds to step 2 in figure 1 .
  • the steel is then cooled until the hottest part of the steel reaches the maximum temperature T max which is lower than the martensitic transformation end temperature in cooling M F 'of the interdendritic spaces, and is then heated immediately. steel.
  • the steel is then immediately subjected to a second treatment of income, substantially identical to the first treatment of income, then allowing the steel to cool to room temperature T A.
  • This second income treatment corresponds to step 3 in figure 1 .
  • the inventors have carried out machinability tests on stainless martensitic steels having undergone the process of the invention. They compared the results of these tests to the results of machinability tests on austenized steels followed by quenching and two incomes but where the minimum temperature of the hottest part of the part is simply less than the martensitic transformation end temperature in cooling M F of the dendrites, and the steel is not immediately warmed between tempering and first income, or between first income and second income.
  • the wear of the machining plates per meter of machined steel is divided by about 10 (11 mm to 1.3 mm cutting speed of 120 m / min compared to a steel manufactured according to a method of the prior art.
  • the power required for machining is further divided by more than two compared to a steel manufactured according to a method of the prior art.
  • the surface condition of the steel after machining is also improved.
  • the results can be explained as follows: as indicated above, the martensitic transformation end temperature in cooling M F 'of the interdendritic regions is less than the martensitic transformation end of cooling temperature M F dendrites. Now we have seen that during the cooling of steel, this steel solidifies into a microstructure which is an alternation of dendrites and interdendritic regions ( figure 2 ). Thus, when the temperature drops below the martensitic transformation end temperature in M F cooling of the dendrites, the dendrites have become martensite, while the interdendritic regions have not yet been transformed into martensite.
  • zones in all the steel ie the interdendritic regions
  • residual austenite Part of this residual austenite will be transformed at the next first income stage into fresh martensite.
  • the other part of this residual austenite will be located only at the most segregated points of the material (for example, in the most concentrated interdendritic spaces).
  • the new fresh martensite stabilizes but another portion of the remaining residual austenite continues to turn into fresh martensitic in these most segregated areas.
  • Steel therefore has a structural heterogeneity with harder grains corresponding to fresh martensite in a softer matrix. It is this heterogeneity that is responsible for the bad machinability of steel, the harder grains using platelets and blocking their advance.
  • the maximum temperature T max that reaches the hottest part of the steel before being reheated is between 20 ° C and 75 ° C.
  • Such a temperature T m is lower than the martensitic transformation end temperature in cooling M F 'interdendritic spaces.
  • this maximum temperature T max is between 28 ° C and 35 ° C.
  • step ( ⁇ ) In order to determine when the hottest part of the steel reaches the maximum temperature T max , it is possible for example, in step ( ⁇ ), to measure the skin temperature of the steel and to use abacuses to deduce the temperature of the hottest part of the steel.
  • the temperature gradient between the surface of the steel and the hottest part of the steel is as small as possible in order to reduce the gap between the end temperature of the steel martensitic transformation in M F cooling of dendrites and martensitic transformation end temperature in cooling M F 'interdendritic spaces. Indeed, by reducing this gap, the constraints in the room are then lower, and we gain in productivity.
  • the threshold duration d s depends on the geometry of the part.
  • the length of s is at least 15 minutes (min) to a minimum dimension of the part of 50 mm, 30 min to a minimum dimension of the part of 100 mm, 45 min to a minimum dimension of the workpiece 150 mm, and so on.
  • d s (15 min) ⁇ ⁇ minimum dimension (in mm) ⁇ / 50.
  • the steel can for example be placed in an oven where a temperature of between T min and MF' prevails.
  • the steel can be thermally insulated from the outside environment, for example by placing it in a blanket.
  • At least one expansion of the steel is performed at a temperature below the temperature of income T R at which the first income and the second income have been made.
  • This relaxation corresponds to step 4 in figure 1 . It allows the relaxation of residual stresses within the steel, and improves the service life.
  • the ESR process consists in placing a steel ingot in a crucible in which a slag (mineral mixture, for example lime, fluoride, magnesia, alumina, spath) has been poured in such a way that the lower end of the ingot quenches in the slag . Then an electric current is passed into the ingot, which serves as an electrode. This stream liquefies the slag and melts the lower end of this electrode which is in contact with the slag. The molten steel of this electrode passes through the slag in the form of fine droplets, to solidify below the layer of supernatant slag, into a new ingot that grows gradually.
  • a slag mineral mixture, for example lime, fluoride, magnesia, alumina, spath
  • the slag acts, inter alia, as a filter which extracts the inclusions from the steel droplets, so that the steel of this new ingot located below the slag layer contains fewer inclusions than the initial ingot (electrode). .
  • This operation is carried out at atmospheric pressure and air.
  • the VAR process consists in melting in a crucible under a high vacuum the steel ingot, which serves as an electrode.
  • the ingot / electrode is melted by establishing an electric arc between the end of the ingot / electrode and the top of the secondary ingot which is formed by melting the ingot / electrode.
  • the secondary ingot solidifies in contact with the walls of the crucible and the inclusions float on the surface of the secondary ingot, and may subsequently be removed. A secondary ingot of greater purity than the initial ingot / electrode is thus obtained.
  • the steel undergoes, before step (1), a reflow.
  • reflow is chosen from a group comprising ESR slag remelting or VAR vacuum arc remelting.
  • step (1) a homogenization treatment of the steel is carried out.
  • the inventors have found that satisfactory results are obtained when the ingot is subjected in this oven to a homogenization treatment during a holding time t after the temperature of the most The cold of this ingot has reached a homogenization temperature T, this time t being equal to at least one hour, and the homogenization temperature T varying between a lower temperature T inf and the burn temperature of this steel.
  • the temperature T inf is approximately equal to 900 ° C.
  • the burn temperature of a steel is defined as the temperature in the raw state of solidification at which the grain boundaries in the steel transform (or even liquefy), and is greater than T Inf . This time t of maintaining the steel in the furnace therefore varies inversely with this homogenization temperature T.
  • the homogenization temperature T is 950 ° C., and the corresponding holding time t is equal to 70 hours.
  • the homogenization temperature T is 1250C which is slightly lower than burn temperature, then the corresponding holding time t is equal to 10 hours.
  • the maximum temperature T max is lower than the martensitic transformation end temperature in cooling M F of the dendrites in the steel, and in steps (1) and (2) it is ensured that steel remains at or below the maximum temperature T max for as short a time as possible.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP11773051.5A 2010-09-14 2011-09-08 Optimisation de l'usinabilite d'aciers martensitiques inoxydables Active EP2616561B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR1057326A FR2964668B1 (fr) 2010-09-14 2010-09-14 Optimisation de l'usinabilite d'aciers martensitiques inoxydables
PCT/FR2011/052056 WO2012035240A1 (fr) 2010-09-14 2011-09-08 Optimisation de l'usinabilite d'aciers martensitiques inoxydables

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EP2616561A1 EP2616561A1 (fr) 2013-07-24
EP2616561B1 true EP2616561B1 (fr) 2016-03-02

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US (1) US9464336B2 (ru)
EP (1) EP2616561B1 (ru)
CN (1) CN103097555B (ru)
BR (1) BR112013006063B1 (ru)
CA (1) CA2810781C (ru)
FR (1) FR2964668B1 (ru)
RU (1) RU2598427C2 (ru)
WO (1) WO2012035240A1 (ru)

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JP5807630B2 (ja) 2012-12-12 2015-11-10 Ｊｆｅスチール株式会社 継目無鋼管の熱処理設備列および高強度ステンレス鋼管の製造方法
FR3013738B1 (fr) * 2013-11-25 2016-10-14 Aubert & Duval Sa Acier inoxydable martensitique, piece realisee en cet acier et son procede de fabrication
JP6918238B2 (ja) * 2018-06-13 2021-08-11 日鉄ステンレス株式会社 マルテンサイト系ｓ快削ステンレス鋼
CN113265512B (zh) * 2021-05-17 2022-08-12 山西太钢不锈钢股份有限公司 一种消除电渣马氏体锻圆机加工表面色差的方法
CN114774650B (zh) * 2022-04-06 2024-08-27 成都先进金属材料产业技术研究院股份有限公司 叶片钢1Cr12Ni3Mo2VN的热处理方法
CN116377314B (zh) * 2023-06-05 2023-10-27 成都先进金属材料产业技术研究院股份有限公司 一种燃气轮机用马氏体耐热钢及其冶炼方法

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US6090230A (en) * 1996-06-05 2000-07-18 Sumitomo Metal Industries, Ltd. Method of cooling a steel pipe
RU2176674C1 (ru) * 2001-03-01 2001-12-10 Федеральное государственное унитарное предприятие Центральный научно-исследовательский институт конструкционных материалов "Прометей" Способ термической обработки высокопрочных коррозионно-стойких хромоникелевых сталей мартенситного класса
FR2872825B1 (fr) * 2004-07-12 2007-04-27 Industeel Creusot Acier inoxydable martensitique pour moules et carcasses de moules d'injection
FR2893954B1 (fr) * 2005-11-29 2008-02-29 Aubert & Duval Soc Par Actions Acier pour outillage a chaud, et piece realisee en cet acier et son procede de fabrication
DE602008003811D1 (de) * 2007-07-10 2011-01-13 Aubert & Duval Sa Gehärteter martensitischer stahl mit geringem oder ohne kobaltanteil, verfahren zur herstellung eines teils aus diesem stahl und in diesem verfahren hergestelltes teil
US8120325B2 (en) * 2007-08-10 2012-02-21 Sony Ericsson Mobile Communications Ab Battery short circuit monitoring
FR2920784B1 (fr) * 2007-09-10 2010-12-10 Aubert & Duval Sa Acier inoxydable martensitique, procede de fabrication de pieces realisees en cet acier et pieces ainsi realisees
FR2951198B1 (fr) * 2009-10-12 2013-05-10 Snecma Traitements thermiques d'aciers martensitiques inoxydables apres refusion sous laitier

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Publication number Publication date
BR112013006063B1 (pt) 2019-02-19
WO2012035240A1 (fr) 2012-03-22
FR2964668B1 (fr) 2012-10-12
RU2598427C2 (ru) 2016-09-27
BR112013006063A2 (pt) 2016-06-07
EP2616561A1 (fr) 2013-07-24
RU2013116810A (ru) 2014-10-20
US9464336B2 (en) 2016-10-11
CN103097555A (zh) 2013-05-08
CA2810781C (fr) 2018-11-06
CN103097555B (zh) 2015-02-18
FR2964668A1 (fr) 2012-03-16
US20130180628A1 (en) 2013-07-18
CA2810781A1 (fr) 2012-03-22

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