US20070053784A1 - Maraging steel article and method of manufacture - Google Patents

Maraging steel article and method of manufacture Download PDF

Info

Publication number
US20070053784A1
US20070053784A1 US11/218,618 US21861805A US2007053784A1 US 20070053784 A1 US20070053784 A1 US 20070053784A1 US 21861805 A US21861805 A US 21861805A US 2007053784 A1 US2007053784 A1 US 2007053784A1
Authority
US
United States
Prior art keywords
article
max
maraging
hrc
weight percent
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.)
Abandoned
Application number
US11/218,618
Other languages
English (en)
Inventor
Joseph Muha
Andrzej Wojcieszynski
Brian McTiernan
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ATI POWDER METALS LLC
ATI Inc
Original Assignee
Crucible Materials Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Crucible Materials Corp filed Critical Crucible Materials Corp
Priority to US11/218,618 priority Critical patent/US20070053784A1/en
Assigned to CRUCIBLE MATERIALS CORPORATION reassignment CRUCIBLE MATERIALS CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MCTIERNAN, BRIAN J., MUHA, JOSEPH F., WOJCIESZYNSKI, ANDRZEJ L.
Priority to MX2008003062A priority patent/MX2008003062A/es
Priority to PL06789641T priority patent/PL1920079T3/pl
Priority to PT06789641T priority patent/PT1920079E/pt
Priority to JP2008529062A priority patent/JP5289956B2/ja
Priority to SI200630350T priority patent/SI1920079T1/sl
Priority to ES06789641T priority patent/ES2357612T3/es
Priority to AT06789641T priority patent/ATE431437T1/de
Priority to EP06789641A priority patent/EP1920079B1/en
Priority to PCT/US2006/031111 priority patent/WO2007030256A1/en
Priority to KR1020087008257A priority patent/KR101315663B1/ko
Priority to CN2006800323815A priority patent/CN101258259B/zh
Priority to CA2620209A priority patent/CA2620209C/en
Priority to UAA200802888A priority patent/UA89842C2/ru
Priority to DE602006006844T priority patent/DE602006006844D1/de
Priority to DK06789641T priority patent/DK1920079T3/da
Publication of US20070053784A1 publication Critical patent/US20070053784A1/en
Priority to HK08112415.4A priority patent/HK1119207A1/xx
Priority to CY20091100769T priority patent/CY1109236T1/el
Assigned to COMPACTION & RESEARCH ACQUISITION LLC reassignment COMPACTION & RESEARCH ACQUISITION LLC ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: CRUCIBLE MATERIALS CORPORATION
Assigned to ATI POWDER METALS LLC reassignment ATI POWDER METALS LLC CHANGE OF NAME (SEE DOCUMENT FOR DETAILS). Assignors: COMPACTION & RESEARCH ACQUISITION LLC
Assigned to Allegheny Technologies Incorporated reassignment Allegheny Technologies Incorporated ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: CRUCIBLE MATERIALS CORPORATION
Assigned to COMPACTION & RESEARCH ACQUISITION LLC reassignment COMPACTION & RESEARCH ACQUISITION LLC ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: CRUCIBLE MATERIALS CORPORATION
Priority to US13/403,368 priority patent/US20120230859A1/en
Abandoned legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22C—FOUNDRY MOULDING
    • B22C9/00—Moulds or cores; Moulding processes
    • B22C9/06—Permanent moulds for shaped castings
    • B22C9/061—Materials which make up the mould
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/007—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of moulds
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the invention relates to the manufacture of a maraging steel article with a specific composition using a powder metallurgy processing method.
  • the steel as produced by practicing this invention is appropriate for applications involving high temperatures or cyclic heating and cooling.
  • the steel article of the invention has a hardness of less than 40 HRC after manufacturing and after solution heat treating, allowing the article to be machined. However, after the manufacture of the article and the subsequent maraging treatment, its hardness is greater than 45 HRC.
  • the applications for the steel article of the invention include processing of plastics or of liquid or hot solid metals, which include but are not limited to mold dies for the casting of liquid metals, mold dies for plastics, dies for forging other metals and dies for extruding.
  • the cyclical heating and cooling of tools for these applications characterize these applications. This cyclical heating and cooling create sufficient stresses in the tool to cause thermal fatigue cracking, also known as heat checking. Different applications can tolerate different amounts of heat checking. For some products that require a high quality cosmetic appearance, the dies must be replaced after very limited heat checking has occurred. For other products that may not require this high quality cosmetic appearance, the dies can be used even with severe heat checking. In all cases, the majority of dies eventually fail and are replaced due to thermal fatigue cracking.
  • Tools are used in several applications involving the processing of hot metal.
  • This metal can be in the liquid form, as in die-casting, or in the solid form, as in hot extrusion and hot forging.
  • the useful life of all these tool materials is typically limited by thermal fatigue cracking. That is, as the process proceeds, more thermal fatigue cracks initiate on the surface of the tool, and existing thermal fatigue cracks grow. The die is replaced when the extent of thermal fatigue cracking renders the produced part as being of unacceptable quality.
  • Requirements of steel used for high temperature applications include:
  • the material must have the capability to be heat-treated to greater than 45 HRC, which is the typical minimum working hardness for most tools of the prior art to maintain shape.
  • the material must also exhibit good high temperature strength. Fatigue cracking is related to the strength of the material. Therefore, a higher strength is one factor that can improve the resistance to thermal fatigue cracking.
  • Thermal fatigue cracking has similarities to conventional fatigue cracking. However, in the case of thermal fatigue cracking, the stresses are introduced in the tool by cyclic heating and cooling. Therefore, it is important that material for such a tool exhibit good resistance to thermal fatigue cracking.
  • the material should have as low a coefficient of thermal expansion as possible or at minimum lower than the current materials in use.
  • the die material must be capable of being coated by PVD (physical vapor deposition) or other relevant coating.
  • the H series tool steels were developed for these applications, with the most common being the 5Cr hot work tool steels.
  • the H13 steel class is nominally in weight percent 0.38 carbon, 5.25 chromium, 1.25 molybdenum, 1.0 silicon and 1.0 vanadium.
  • the H11 steel class is essentially the same as the H13 class but with weight percent 0.5 vanadium.
  • the H11 or H13 steel is typically processed using electro slag remelting (ESR) or vacuum arc remelting (VAR) methods.
  • ESR electro slag remelting
  • VAR vacuum arc remelting
  • maraging steels Most of them contain approximately 18% nickel and some titanium and obtain their hardness by precipitation of Ni—Mo and Ni—Ti particles. Many of these steels are aged using a relatively low temperature, typically less than
  • the invention provides a new powder metallurgy produced maraging steel alloy article to be used as a tool for high temperature applications that satisfies the above-stated requirements.
  • the article is fully dense and of prealloyed powder particles.
  • Hardening of the material is achieved by solution annealing and ageing, i.e. heating at a prescribed temperature for a prescribed length of time. This allows small precipitate particles to form, which in turn harden the low carbon martensitic structure of the material.
  • Molybdenum is a key element in the strengthening of this maraging steel, as the precipitate responsible for hardening the alloy is Fe 2 Mo. It is also a key element in increasing the temper resistance of the alloy. Excessive quantities of molybdenum can allow the formation of detrimental delta ferrite.
  • Cobalt is required in a proper balance to prevent undesirable phases and to influence the aging process.
  • Cobalt is an austenite former while preventing the formation of delta ferrite at high temperatures and has a minimal effect on the austenite to martensite transformation temperature.
  • Cobalt also lowers the solubility of molybdenum in the martensitic matrix, thus making molybdenum more available for precipitation.
  • Chromium is desirable in some quantity for resistance to high temperature oxidation. Chromium in excessive quantity can result in the formation of delta ferrite.
  • Nickel also provides some benefit to oxidation resistance and is beneficial to mechanical properties. Excess nickel can cause the formation of austenite at typical service temperatures.
  • Carbon is not a critical element in the strengthening mechanism of this material.
  • Silicon is not a critical element in the properties of the alloy. Silicon may be used for deoxidizing during melting. It is a strong ferrite stabilizer.
  • Manganese is not critical for the properties of this alloy. It can be used to form manganese sulfide and therefore the content should be increased with increasing quantities of sulfur for enhanced machinability.
  • Sulfur may be present to promote machinability.
  • Vanadium, niobium, titanium, tungsten, zirconium, aluminum and other strong carbide and/or nitride formers are elements that are not desired and therefore should not exist in amounts above incidental impurity levels.
  • the alloy article of the invention is provided in the solution-annealed condition, which is performed by heating the material between 1740° F. and 1925° F. Hardening by maraging is achieved by heating the material between 1050° F. and 1360° F.
  • FIG. 1 is a graph showing the comparison of an alloy specimen within the composition limits of the invention produced by powder metallurgy and one produced by ESR with respect to ductility;
  • FIG. 2 is a graph comparing the thermal fatigue resistance of a specimen in accordance with the invention and a specimen of H13 alloy.
  • FIG. 3 is a graph comparing hardness of a specimen in accordance with the invention and a specimen of H13 alloy.
  • the rapid strain tensile testing was performed using the alloy article of the invention produced by powder metallurgy and electro slag remelted material of the same composition.
  • the specimens were heated by direct resistance heating. After achieving and equalizing at the desired test temperature, a load was applied to achieve a strain rate of 550 in/in/minute. This test is useful in simulating the conditions that exist during the hot working of the material.
  • FIG. 1 shows the reduction in area of the rapid strain rate tensile test for the specimens produced of the alloy of invention and the ESR material of the same composition. This clearly shows a substantial ductility advantage for the powder metallurgy material. The ductility of the ESR material was insufficient to permit hot working.
  • thermal fatigue resistance Another important characteristic of hot work tool steels is thermal fatigue resistance.
  • thermal fatigue cracking There are several tests available to measure thermal fatigue cracking, although none of these tests are a standard method (e.g. ASTM). Some testing is performed by heating a specimen to a high temperature using an induction coil for heating, then allowing the specimen to cool. This is performed over a number of cycles, with the specimen being evaluated periodically during the test.
  • Another method involves testing a specimen with an internal cooling cavity for cooling water. This specimen is repeatedly immersed into a liquid aluminum bath. Again the cracking is rated periodically during the test.
  • the testing for the alloy of the invention was performed using a 1 ⁇ 2′′ square by 6′′ long solid specimen produced by hot isostatic pressing and hot working.
  • the test specimen can be tested simultaneously with up to five other specimens during the same procedure.
  • the other specimen for this experiment was an ESR H13 material, which is the alloy most frequently used in aluminum die casting dies.
  • the specimens were bolted to a holding plate affixed to the end of a mechanical arm which moved the specimens through the various stages of the test cycle.
  • the arm immersed the specimens into molten aluminum to a depth of approximately 5 inches for 7 seconds.
  • the specimens were then lifted out of the molten aluminum, moved to a position above a tank of water and then immersed into the water for 12 seconds.
  • the specimens were then lifted out of the water, and the arm moved to a position above the molten aluminum for 5 seconds to dry the specimens.
  • the cycle was then repeated.
  • the specimens were periodically evaluated for thermal fatigue cracking, typically every 5,000 cycles.
  • Two opposite faces of the specimens were cleaned using silicon carbide paper on a granite surface plate.
  • the four cleaned corners of each specimen were then examined under a stereo microscope at a magnification of 90 ⁇ .
  • the examinations were conducted in an area 13 ⁇ 8′′ long, and which was located about 13 ⁇ 8′′ from the bottom end of the specimens.
  • FIG. 2 is a graphic representation of trial results of the powder metallurgy produced invention specimen versus the ESR H13 steel specimen. As previously discussed, thermal fatigue cracking is the most frequent cause of tool failure. For this reason, it is believed that thermal fatigue testing provides the most important indication of the improved performance of the alloy of invention.
  • FIG. 3 is a graphical representation of the hardness level as a function of hold time at 1200° F. It can be seen that the alloy of the invention has a superior temper resistance to H13 steel.
  • Table 4 shows the results of tensile testing of the PM alloy article of the invention versus results for ESR H13 steel. Specimens tested were machined to a 0.250′′ diameter with a 1.00′′ gage length (4D). The results indicate that the alloy of invention has a higher yield and tensile strength at both room temperature and at 1000° F. This higher strength makes the alloy article of the invention less susceptible to thermal fatigue cracking.
  • TABLE 4 Tensile Properties Invention Maraging ESR H13 Steel Article (47 HRC) (45 HRC) 72° F.
  • Thermal expansion is an important factor, both in the resistance of a tool to thermal fatigue cracking and in the final product quality of a tool. In both cases, a smaller coefficient of thermal expansion is desired.
  • the significance of the lower coefficient of thermal expansion is that with less dimensional change, the tool will be subjected to lower thermal stresses than a material with a greater dimensional change. The lower stresses present will thus render the tool more resistant to thermal fatigue cracking.
  • the coefficient of thermal expansion was determined by the thermal dilatometric analysis (TDA) method.
  • TDA thermal dilatometric analysis
  • the coefficient of thermal expansion for the PM alloy article of the invention was determined to be 6.6 ⁇ 10 ⁇ 6 in./in./° F. over the temperature range of 72° F. to 1110° F.
  • the ESR H13 die steel had a coefficient of 7.3 ⁇ 10 ⁇ 6 in./in./° F. over the temperature range of 72° F. to 1110° F.
  • the PM invention alloy article is easily coated with either a physical vapor deposition (PVD) process or chemical vapor deposition (CVD) which employs a higher temperature than the PVD process.
  • PVD physical vapor deposition
  • CVD chemical vapor deposition
  • the alloy article of the invention was coated with TiN, TiAlN and CrN PVD coatings.
  • the coatings were deposited at a high deposition rate at a temperature range of 750-850° F. for both the article of the invention and ESR H13 steel. Unlike many other maraging steels, this temperature is well below the aging temperature for the alloy article of the invention.
  • the coating was deposited using a chemical vapor deposition process on both the alloy article of the invention and conventional tool steel material.
  • Conventional tool steels are not well suited for CVD, as the coating process typically takes place at a temperature above the critical temperature of these alloys.
  • the advantage provided by the article of the invention is that the CVD process results in the required heat treatment, namely solution annealing. After coating, the invention article requires only a single aging treatment. The nature of the maraging process is such that the dimensional changes of the tool are very minimal, allowing for good adherence of the coating to the substrate.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Steel (AREA)
US11/218,618 2005-09-06 2005-09-06 Maraging steel article and method of manufacture Abandoned US20070053784A1 (en)

Priority Applications (19)

Application Number Priority Date Filing Date Title
US11/218,618 US20070053784A1 (en) 2005-09-06 2005-09-06 Maraging steel article and method of manufacture
DK06789641T DK1920079T3 (da) 2005-09-06 2006-08-10 Höjtlegeret (maraging) stålgenstand og tilhörende fremstillingsmetode
KR1020087008257A KR101315663B1 (ko) 2005-09-06 2006-08-10 마레이징강 물품 및 제조방법
CA2620209A CA2620209C (en) 2005-09-06 2006-08-10 A maraging steel article and method of manufacture
PT06789641T PT1920079E (pt) 2005-09-06 2006-08-10 Artigo de aço martensítico envelhecido e método de fabrico
JP2008529062A JP5289956B2 (ja) 2005-09-06 2006-08-10 マルエージング鋼物品および製造方法
SI200630350T SI1920079T1 (sl) 2005-09-06 2006-08-10 Izdelek iz maraging jekla in postopek izdelave
ES06789641T ES2357612T3 (es) 2005-09-06 2006-08-10 Un artículo de acero martensítico envejecido y método de fabricación.
AT06789641T ATE431437T1 (de) 2005-09-06 2006-08-10 Gegenstand aus maraging-stahl und zugehöriges herstellungsverfahren
EP06789641A EP1920079B1 (en) 2005-09-06 2006-08-10 A maraging steel article and method of manufacture
PCT/US2006/031111 WO2007030256A1 (en) 2005-09-06 2006-08-10 A maraging steel article and method of manufacture
MX2008003062A MX2008003062A (es) 2005-09-06 2006-08-10 Articulo de acero endurecido por precipitacion de martensita y metodo de fabricacion.
CN2006800323815A CN101258259B (zh) 2005-09-06 2006-08-10 马氏体时效钢制品及制备方法
PL06789641T PL1920079T3 (pl) 2005-09-06 2006-08-10 Wyrób ze stali starzonej w stanie martenzytycznym i sposób wytwarzania
UAA200802888A UA89842C2 (ru) 2005-09-06 2006-08-10 ИЗДЕЛИЕ ИЗ БЕЗПОРИСТОИ мартенситно-Стареющей СТАЛИ И СПОСОБ ЕГО ИЗГОТОВЛЕНИЯ
DE602006006844T DE602006006844D1 (de) 2005-09-06 2006-08-10 Gegenstand aus maraging-stahl und zugehöriges herstellungsverfahren
HK08112415.4A HK1119207A1 (en) 2005-09-06 2008-11-13 A maraging steel article and method of manufacture
CY20091100769T CY1109236T1 (el) 2005-09-06 2009-07-20 Αντικειμενο χαλυβα μαρτενσιτικης γηρανσης και μεθοδος βιομηχανικης κατασκευης
US13/403,368 US20120230859A1 (en) 2005-09-06 2012-02-23 Maraging steel article and method of manufacture

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
US11/218,618 US20070053784A1 (en) 2005-09-06 2005-09-06 Maraging steel article and method of manufacture

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US13/403,368 Continuation US20120230859A1 (en) 2005-09-06 2012-02-23 Maraging steel article and method of manufacture

Publications (1)

Publication Number Publication Date
US20070053784A1 true US20070053784A1 (en) 2007-03-08

Family

ID=37434148

Family Applications (2)

Application Number Title Priority Date Filing Date
US11/218,618 Abandoned US20070053784A1 (en) 2005-09-06 2005-09-06 Maraging steel article and method of manufacture
US13/403,368 Abandoned US20120230859A1 (en) 2005-09-06 2012-02-23 Maraging steel article and method of manufacture

Family Applications After (1)

Application Number Title Priority Date Filing Date
US13/403,368 Abandoned US20120230859A1 (en) 2005-09-06 2012-02-23 Maraging steel article and method of manufacture

Country Status (18)

Country Link
US (2) US20070053784A1 (zh)
EP (1) EP1920079B1 (zh)
JP (1) JP5289956B2 (zh)
KR (1) KR101315663B1 (zh)
CN (1) CN101258259B (zh)
AT (1) ATE431437T1 (zh)
CA (1) CA2620209C (zh)
CY (1) CY1109236T1 (zh)
DE (1) DE602006006844D1 (zh)
DK (1) DK1920079T3 (zh)
ES (1) ES2357612T3 (zh)
HK (1) HK1119207A1 (zh)
MX (1) MX2008003062A (zh)
PL (1) PL1920079T3 (zh)
PT (1) PT1920079E (zh)
SI (1) SI1920079T1 (zh)
UA (1) UA89842C2 (zh)
WO (1) WO2007030256A1 (zh)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7722246B1 (en) * 2005-04-20 2010-05-25 Carty William M Method for determining the thermal expansion coefficient of ceramic bodies and glazes
US20130065073A1 (en) * 2010-05-25 2013-03-14 Panasonic Corporation Metal powder for selective laser sintering, method for manufacturing three-dimensional shaped object by using the same, and three-dimensional shaped object obtained therefrom
SE1751249A1 (en) * 2017-10-09 2019-04-10 Uddeholms Ab Steel suitable for hot working tools
CN113414404A (zh) * 2021-05-21 2021-09-21 西安建筑科技大学 一种增材制造h13钢的方法
CN114351048A (zh) * 2021-12-20 2022-04-15 广东省科学院中乌焊接研究所 一种马氏体时效钢粉末及在增材制造中应用
US20220162729A1 (en) * 2020-11-26 2022-05-26 Hyundai Motor Company Self-healing alloy and method for manufacturing the same
EP4240883A4 (en) * 2020-11-05 2024-04-03 Uddeholms Ab MARAGING STEEL

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20070053784A1 (en) * 2005-09-06 2007-03-08 Crucible Materials Corp. Maraging steel article and method of manufacture
BR112014020919B1 (pt) * 2012-02-24 2020-10-27 Dsm Ip Assets B.V sistema catalítico em pó para processos de hidrogenação
CN110280764A (zh) * 2019-07-22 2019-09-27 陕西科技大学 一种基于slm成型件的马氏体时效钢及其制备方法
CN114480943A (zh) * 2021-12-14 2022-05-13 湖南英捷高科技有限责任公司 一种超低碳低钴马氏体钢及其制备方法
NO347610B1 (en) 2022-05-19 2024-01-29 Hydro Extruded Solutions As A method of producing a die for extrusion of aluminium profiles, and an extrusion die

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5447800A (en) * 1993-09-27 1995-09-05 Crucible Materials Corporation Martensitic hot work tool steel die block article and method of manufacture
US5482531A (en) * 1993-12-07 1996-01-09 Crucible Materials Corporation Titanium-free, nickel-containing maraging steel die block article and method of manufacture
US5599404A (en) * 1992-11-27 1997-02-04 Alger; Donald L. Process for forming nitride protective coatings
US20050187056A1 (en) * 2004-02-24 2005-08-25 Yucong Wang CVT belt with chromium nitride coating
US20120230859A1 (en) * 2005-09-06 2012-09-13 Ati Powder Metals Llc Maraging steel article and method of manufacture

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5110171B1 (zh) * 1967-06-13 1976-04-02
JPS5161B1 (zh) * 1967-09-18 1976-01-05
US5435824A (en) * 1993-09-27 1995-07-25 Crucible Materials Corporation Hot-isostatically-compacted martensitic mold and die block article and method of manufacture
CN1182141A (zh) * 1996-11-13 1998-05-20 哈尔滨工业大学 少镍无钴马氏体时效钢
KR100374980B1 (ko) * 1999-02-12 2003-03-06 히다찌긴조꾸가부시끼가이사 우수한 기계가공성을 갖는 다이스용 고장력강

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5599404A (en) * 1992-11-27 1997-02-04 Alger; Donald L. Process for forming nitride protective coatings
US5447800A (en) * 1993-09-27 1995-09-05 Crucible Materials Corporation Martensitic hot work tool steel die block article and method of manufacture
US5482531A (en) * 1993-12-07 1996-01-09 Crucible Materials Corporation Titanium-free, nickel-containing maraging steel die block article and method of manufacture
US20050187056A1 (en) * 2004-02-24 2005-08-25 Yucong Wang CVT belt with chromium nitride coating
US20120230859A1 (en) * 2005-09-06 2012-09-13 Ati Powder Metals Llc Maraging steel article and method of manufacture

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7722246B1 (en) * 2005-04-20 2010-05-25 Carty William M Method for determining the thermal expansion coefficient of ceramic bodies and glazes
US20130065073A1 (en) * 2010-05-25 2013-03-14 Panasonic Corporation Metal powder for selective laser sintering, method for manufacturing three-dimensional shaped object by using the same, and three-dimensional shaped object obtained therefrom
US8828116B2 (en) * 2010-05-25 2014-09-09 Panasonic Corporation Metal powder for selective laser sintering, method for manufacturing three-dimensional shaped object by using the same, and three-dimensional shaped object obtained therefrom
SE1751249A1 (en) * 2017-10-09 2019-04-10 Uddeholms Ab Steel suitable for hot working tools
WO2019074427A1 (en) * 2017-10-09 2019-04-18 Uddeholms Ab STEEL APPROPRIATE FOR HOT FORMING TOOLS
SE541309C2 (en) * 2017-10-09 2019-06-25 Uddeholms Ab Steel suitable for hot working tools
EP4240883A4 (en) * 2020-11-05 2024-04-03 Uddeholms Ab MARAGING STEEL
US20220162729A1 (en) * 2020-11-26 2022-05-26 Hyundai Motor Company Self-healing alloy and method for manufacturing the same
US11913098B2 (en) * 2020-11-26 2024-02-27 Hyundai Motor Company Self-healing alloy and method for manufacturing the same
CN113414404A (zh) * 2021-05-21 2021-09-21 西安建筑科技大学 一种增材制造h13钢的方法
CN114351048A (zh) * 2021-12-20 2022-04-15 广东省科学院中乌焊接研究所 一种马氏体时效钢粉末及在增材制造中应用

Also Published As

Publication number Publication date
JP5289956B2 (ja) 2013-09-11
CN101258259A (zh) 2008-09-03
CN101258259B (zh) 2010-11-10
PT1920079E (pt) 2009-06-26
CA2620209C (en) 2015-05-05
CA2620209A1 (en) 2007-03-15
DE602006006844D1 (de) 2009-06-25
EP1920079A1 (en) 2008-05-14
ATE431437T1 (de) 2009-05-15
KR20080049097A (ko) 2008-06-03
JP2009507132A (ja) 2009-02-19
SI1920079T1 (sl) 2009-10-31
UA89842C2 (ru) 2010-03-10
CY1109236T1 (el) 2014-07-02
US20120230859A1 (en) 2012-09-13
ES2357612T3 (es) 2011-04-28
HK1119207A1 (en) 2009-02-27
WO2007030256A1 (en) 2007-03-15
MX2008003062A (es) 2008-03-19
KR101315663B1 (ko) 2013-10-08
PL1920079T3 (pl) 2009-09-30
DK1920079T3 (da) 2009-08-17
EP1920079B1 (en) 2009-05-13

Similar Documents

Publication Publication Date Title
CA2620209C (en) A maraging steel article and method of manufacture
EP2152922B1 (en) Nickel-base alloys and articles made therefrom
AU2007283164B2 (en) Process for setting the thermal conductivity of a steel, tool steel, in particular hot-work steel, and steel object
BR112018075617B1 (pt) Aço para preparação de um molde para formação de plásticos, pó pré-formado para formar liga, seu uso, e artigo
KR100562761B1 (ko) 열간 가공툴용 강재료
JPH1096049A (ja) プラスチック材料用金型を製造するための低合金鋼
KR20080073762A (ko) 열간 공구강, 및 이 강으로부터 제조되는 부품, 그 제조방법, 및 그 사용 방법
KR20210006935A (ko) 고강도 티탄 합금
JPH1096048A (ja) プラスチック用金型の製造で用いられる溶接修復可能な鋼
KR101700680B1 (ko) 철-코발트-몰리브덴/텅스텐-질소-합금으로 이루어진 물체들의 제조 방법
EP1722000A1 (en) High strength stainless chromium-nickel steel without aluminium and titanium, and method for making same
WO2018056884A1 (en) Hot work tool steel
US5415834A (en) Warm forging implement, composition and method of manufacture thereof
TW202206620A (zh) 熱加工工具鋼
EP1159463A1 (en) Mould steel
KR100672839B1 (ko) 동합금 다이캐스팅 및 고온 소성가공에 사용되는내열ㆍ내산화성의 금형소재 및 그 제조방법
CN116174629A (zh) 一种富镍镍钛合金管材的低成本制备方法及其在球阀上的应用
JP2006341273A (ja) 熱間鍛造金型用肉盛溶接材料及びその溶接材料を用いた熱間鍛造用金型
JP2006316325A (ja) 大気中鋳造超高強度ステンレス鋼およびステンレス鋼製鋳造品およびステンレス鋼の鋳造部材を製造する方法
KR20040044048A (ko) 냉열 복합소재 특수강 및 그 제조방법
CN108048751A (zh) 一种耐高温模具及其制备方法

Legal Events

Date Code Title Description
AS Assignment

Owner name: CRUCIBLE MATERIALS CORPORATION, NEW YORK

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:MUHA, JOSEPH F.;WOJCIESZYNSKI, ANDRZEJ L.;MCTIERNAN, BRIAN J.;REEL/FRAME:016961/0869

Effective date: 20050509

AS Assignment

Owner name: COMPACTION & RESEARCH ACQUISITION LLC, PENNSYLVANI

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION;REEL/FRAME:023486/0068

Effective date: 20091022

Owner name: ATI POWDER METALS LLC, PENNSYLVANIA

Free format text: CHANGE OF NAME;ASSIGNOR:COMPACTION & RESEARCH ACQUISITION LLC;REEL/FRAME:023486/0089

Effective date: 20091027

AS Assignment

Owner name: ALLEGHENY TECHNOLOGIES INCORPORATED,PENNSYLVANIA

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION;REEL/FRAME:023937/0882

Effective date: 20091022

Owner name: ALLEGHENY TECHNOLOGIES INCORPORATED, PENNSYLVANIA

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION;REEL/FRAME:023937/0882

Effective date: 20091022

AS Assignment

Owner name: COMPACTION & RESEARCH ACQUISITION LLC,PENNSYLVANIA

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION;REEL/FRAME:024160/0493

Effective date: 20091022

Owner name: COMPACTION & RESEARCH ACQUISITION LLC, PENNSYLVANI

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:CRUCIBLE MATERIALS CORPORATION;REEL/FRAME:024160/0493

Effective date: 20091022

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION