US20150275340A1 - Dual-phase stainless steel - Google Patents

Dual-phase stainless steel Download PDF

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Publication number
US20150275340A1
US20150275340A1 US14/231,778 US201414231778A US2015275340A1 US 20150275340 A1 US20150275340 A1 US 20150275340A1 US 201414231778 A US201414231778 A US 201414231778A US 2015275340 A1 US2015275340 A1 US 2015275340A1
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Prior art keywords
dual
stainless steel
phase
article
manufacture
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US14/231,778
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David C. Berry
Ronald E. Bailey
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ATI Properties LLC
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ATI Properties LLC
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Priority to US14/231,778 priority Critical patent/US20150275340A1/en
Assigned to ATI PROPERTIES, INC. reassignment ATI PROPERTIES, INC. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BERRY, DAVID C., BAILEY, RONALD E.
Priority to PL15712762T priority patent/PL3126537T3/pl
Priority to EP15712762.2A priority patent/EP3126537B1/en
Priority to RU2016142683A priority patent/RU2721668C2/ru
Priority to JP2016560351A priority patent/JP6621419B2/ja
Priority to MX2016012853A priority patent/MX2016012853A/es
Priority to AU2015241412A priority patent/AU2015241412B2/en
Priority to SI201531308T priority patent/SI3126537T1/sl
Priority to KR1020167028606A priority patent/KR20160140733A/ko
Priority to PCT/US2015/020122 priority patent/WO2015153092A1/en
Priority to CA2944491A priority patent/CA2944491A1/en
Priority to ES15712762T priority patent/ES2808627T3/es
Priority to CN201580018031.2A priority patent/CN106460128A/zh
Priority to TW104110764A priority patent/TWI651419B/zh
Publication of US20150275340A1 publication Critical patent/US20150275340A1/en
Priority to UAA201610885A priority patent/UA119168C2/uk
Assigned to ATI PROPERTIES LLC reassignment ATI PROPERTIES LLC CERTIFICATE OF CONVERSION Assignors: ATI PROPERTIES, INC.
Abandoned legal-status Critical Current

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    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/02—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
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • C21D2211/005—Ferrite
    • 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
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2200/00—Crystalline structure

Definitions

  • the present disclosure relates to a dual-phase stainless steel having a microstructure of ferrite and tempered martensite.
  • the present disclosure relates to cost-effective stainless steels having improved hardness for abrasion-resistant and/or wear-resistant applications.
  • Dual-phase stainless steels can exhibit a combination of desirable properties that make them useful for a wide variety of industrial applications, such as for oil sands extraction and in the sugar industry. These steels are generally characterized by a microstructure of tempered martensite dispersed in a ferrite matrix.
  • ATI 412TM stainless steel typically contains, by weight, 11.75% chromium (Cr), 0.90% manganese (Mn), 0.70% silicon (Si), 0.40% nickel (Ni), 0.030% sulfur (S), 0.020% carbon (C), 0% to 0.040% phosphorus (P), 0% to 0.030% nitrogen (N), and the balance iron (Fe) and other incidental impurities.
  • ATI 412TM stainless steel typically has a Brinell hardness (HB) of about 177 when annealed at about 766° C., and a Brinell hardness of about 258 when annealed at about 843° C.
  • Duracorr® steel which contains, by weight, 11.0% to 12.5% Cr, 0.20% to 0.35% molybdenum (Mo), 0% to 1.50% Mn, 0% to 1.00% Ni, 0% to 0.70% Si, 0% to 0.040% P, 0% to 0.030% N, 0% to 0.025% C, 0% to 0.015% S, and the balance Fe.
  • Mo molybdenum
  • Duracorr® stainless steel contains Mo as an alloying element, i.e., an intentional alloying addition, and not as an incidental impurity. Because of the rising costs of Mo, however, Duracorr® stainless steel may be too costly for certain applications.
  • Duracorr® stainless steel typically has a hardness of about 223 HB, it can be processed to exhibit nominal hardness of 300 HB, which grade is commercially available as Duracorr® 300 stainless steel.
  • Duracorr® and Duracorr® 300 stainless steels have largely the same composition, but the hardness of Duracorr® 300 stainless steel varies from 260 HB to 360 HB.
  • the increased hardness of Duracorr® 300 stainless steel is accompanied by a reduction in toughness.
  • the Charpy V-notch impact energy of Duracorr® 300 stainless steel at ⁇ 40° C. is only about 15 ft-lb on average.
  • high hardness levels for example, up to about 350 HB, may be desirable in combination with higher toughness than is available from Duracorr® 300 stainless steel.
  • an in-service work hardenability up to about 450-500 HB, for example, may be required in certain applications.
  • an embodiment of a high-hardness dual-phase ferritic-martensitic stainless steel is described.
  • the stainless steel comprises, by weight, about 11.5% to about 12% Cr, about 0.8% to about 1.5% Mn, about 0.75% to about 1.5% Ni, 0% to about 0.5% Si, 0% to about 0.2% Mo, 0% to about 0.0025% B, Fe, and impurities.
  • the stainless steel according to the present disclosure exhibits Brinell hardness (HB) and Charpy V-notch impact energy at ⁇ 40° C. (CVN) such that CVN (ft-lb)+(0.4 ⁇ HB) is about 160 or greater.
  • HB Brinell hardness
  • CVN Charpy V-notch impact energy at ⁇ 40° C.
  • an embodiment of an article of manufacture including a high-hardness dual-phase ferritic-martensitic stainless steel is described.
  • the stainless steel comprises, by weight, about 11.5% to about 12% Cr, about 0.8% to about 1.5% Mn, about 0.75% to about 1.5% Ni, 0% to about 0.5% Si, 0% to about 0.2% Mo, 0% to about 0.0025% B, Fe, and impurities.
  • the stainless steel exhibits Brinell hardness (HB) and Charpy V-notch impact energy at ⁇ 40° C. (CVN) such that CVN (ft-lb)+(0.4 ⁇ HB) is about 160 or greater.
  • HB Brinell hardness
  • CVN Charpy V-notch impact energy at ⁇ 40° C.
  • FIG. 1 is a graph plotting Brinell hardness and Charpy V-notch impact energy of non-limiting embodiments of stainless steels according to the present disclosure in comparison to certain conventional steels.
  • the present disclosure is directed to cost-effective dual-phase ferritic-martensitic stainless steels having advantageous hardness and which are suitable for use in various applications requiring abrasion resistance and/or wear resistance.
  • certain embodiments of dual-phase ferritic-martensitic stainless steels according to the present disclosure comprise, by weight, about 11.5% to about 12% Cr, about 0.8% to about 1.5% Mn, about 0.75% to about 1.5% Ni, 0% to about 0.5% Si, 0% to about 0.2% Mo, 0% to about 0.0025% B, Fe, and impurities.
  • the stainless steels exhibit Brinell hardness (HB) and Charpy V-notch impact energy at ⁇ 40° C. (CVN) such that the following is satisfied: CVN (ft-lb)+(0.4 ⁇ HB) is about 160 or greater.
  • Cr may be provided in the alloys of the present disclosure to impart corrosion resistance.
  • a Cr content of about 11.5% (by weight) or more may be required to provide adequate corrosion resistance.
  • excessive Cr may undesirably (1) stabilize the ferrite phase and/or (2) embrittling phases such as the sigma phase.
  • certain embodiments of the stainless steels according to the present disclosure include a Cr content of about 11.5% to about 12%, by weight.
  • Mn may be provided in the alloys of the present disclosure to improve work hardenability.
  • a Mn content of about 0.8% (by weight) or more may be required to achieve the desired work hardening effects.
  • excessive Mn may undesirably segregate during processing of the stainless steels.
  • certain embodiments of the stainless steels according to the present disclosure include a Mn content of about 0.8% to about 1.5%, by weight.
  • the Mn content of the stainless steels may be about 1.0% to about 1.5%, by weight.
  • the addition of Mn in combination with the addition of other alloying elements can advantageously affect work hardenability such that the steels attain a hardness of about 450 HB or greater.
  • Ni may be provided in the alloys of the present disclosure to help stabilize the martensitic phase of the dual-phase (martensitic-ferritic) alloys.
  • a Ni content of about 0.75% by weight or more may be required to provide a material including higher levels of martensite than in Duracorr® 300 stainless steel.
  • the nickel content of the alloys may promote hardness of the alloys' martensite phase by stabilizing austenite formation during heat treatment, allowing more time for carbon diffusion.
  • due to the high cost of Ni it may be desirable to limit the Ni content.
  • some embodiments of the steels according to the present disclosure include a Ni content of about 0.75% to about 1.5% (by weight) to provide a cost-effective dual-phase stainless steel with high hardness levels up to about 350 HB, in combination with higher toughness than is typical of Duracorr® 300 stainless steel.
  • the Ni content of stainless steels according to the present disclosure may be about 1.0% to about 1.5%, by weight.
  • the level of Si may be limited to (1) destabilize the ferritic phase of the dual-phase stainless steels and/or (2) avoid embrittling phases such as the sigma phase. Accordingly, certain embodiments of the steels according to the present disclosure include 0% to no more than about 0.5% Si, by weight.
  • the level of Mo may be limited to (1) destabilize the ferritic phase of the dual-phase stainless steels and/or (2) avoid embrittling phases such as the sigma phase. Accordingly, certain embodiments of the steels according to the present disclosure include 0% to no more than about 0.2% Mo, by weight. In certain other embodiments of the steels according to the present disclosure, the Mo concentration is 0% to no more than about 0.1%, by weight
  • B may be provided in the dual-phase stainless steels of the present disclosure to improve martensite hardness.
  • Certain embodiments of the steels according to the present disclosure include 0% to about 0.0025% B, by weight. In certain embodiments of the steels, the B content may be about 0.002% to about 0.0025%, by weight.
  • Incidental elements and impurities in the disclosed alloys may include, for example, one or more of C, N, P, and S.
  • the total content of these elements is no more than 0.1%, by weight.
  • C may be present in the steels disclosed herein in an amount no more than 0.025%, by weight.
  • S may be present in the steels disclosed herein in an amount no more than 0.01%, by weight.
  • N may be present in the steels disclosed herein in an amount no more than 0.03%, by weight.
  • Incidental levels of various metallic elements also may be present in embodiments of alloys according to the present disclosure.
  • certain non-limiting embodiments of alloys according to the present disclosure may include up to 0.25% copper (Cu), by weight.
  • dual-phase ferritic-martensitic stainless steels comprise by weight: about 11.5% to about 12% Cr; about 1.0% to about 1.5% Mn; about 1.0% to about 1.5% Ni; 0% to about 0.5% Si; 0% to about 0.1% Mo; 0% to about 0.0025% B; 0% to about 0.025% C; 0% to about 0.01% S; 0% to about 0.03% N, Fe, and impurities.
  • the stainless steels further comprise P.
  • the total concentration of C, N, P, and S is no greater than about 0.1%, by weight.
  • the concentration of B in the steels is about 0.002% to about 0.0025%, by weight.
  • the steels include no more than 0.25% Cu, by weight.
  • dual-phase ferritic-martensitic stainless steels consist essentially of, by weight: about 11.5% to about 12% chromium; about 0.8% to about 1.5% manganese; about 0.75% to about 1.5% nickel; 0% to about 0.5% silicon; 0% to about 0.2% molybdenum; 0% to about 0.0025% boron; 0% to about 0.025% carbon; 0% to about 0.01% sulfur; 0% to about 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • dual-phase ferritic-martensitic stainless steels consist essentially of, by weight: about 11.5% to about 12% chromium; about 1.0% to about 1.5% manganese; about 1.0% to about 1.5% nickel; 0% to about 0.5% silicon; 0% to about 0.1% molybdenum; 0% to about 0.0025% boron; 0% to about 0.025% carbon; 0% to about 0.01% sulfur; 0% to about 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • dual-phase ferritic-martensitic stainless steels consist of, by weight: about 11.5% to about 12% chromium; about 0.8% to about 1.5% manganese; about 0.75% to about 1.5% nickel; 0% to about 0.5% silicon; 0% to about 0.2% molybdenum; 0% to about 0.0025% boron; 0% to about 0.025% carbon; 0% to about 0.01% sulfur; 0% to about 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • dual-phase ferritic-martensitic stainless steels consist of, by weight: about 11.5% to about 12% chromium; about 1.0% to about 1.5% manganese; about 1.0% to about 1.5% nickel; 0% to about 0.5% silicon; 0% to about 0.1% molybdenum; 0% to about 0.0025% boron; 0% to about 0.025% carbon; 0% to about 0.01% sulfur; 0% to about 0.03% nitrogen; optionally at least one of copper and phosphorus; iron; and impurities.
  • hardness is generally inversely related to toughness.
  • Brinell hardness (HB) is the primary measure of hardness
  • Charpy V-notch impact energy at ⁇ 40° C. (CVN) is the primary measure of toughness.
  • CVN (ft-lb)+(0.4 ⁇ HB) of the steels is about 160 or greater.
  • hardness is about 300 HB or greater
  • CVN is about 50 ft-lb or greater.
  • the steels according to the present disclosure have an in-service work hardenability up to a hardness of about 450 HB or greater.
  • Table 1 includes the compositions and certain properties of an embodiment of the dual-phase ferritic-martensitic stainless steels according to the present disclosure and of conventional ATI 412TM stainless steel and conventional Duracorr® 300 stainless steel. Heats of the three alloys listed in Table 1 were melted into slabs weighing about 15,000 lb and rolled at a temperature of about 1950° F. to produce material about 6 mm thick. Following the rolling process, the steels were annealed at 766° C. or 843° C., for 15 minutes, and air cooled.
  • the mechanical properties of the experimental steel embodiment listed in Table 1 were measured and compared to those of the two listed conventional steels.
  • the Brinell hardness and CVN at ⁇ 40° C. (ft-lb) are shown in Table 1 for the three alloys.
  • the tensile tests were conducted according to the American Society for Testing and Materials (ASTM) standard A370 at room temperature, using a tungsten carbide ball indenter, on samples measuring about 5 cm in gauge length and about 0.5 cm in thickness.
  • the Charpy tests were conducted according to ASTM standard A370 and E23 at about ⁇ 40° C. on transverse samples measuring about 10 mm ⁇ 2.5 mm. Because these samples are considered subsize per ASTM-A370, the measured impact energy was converted to standard size specimen values in Table 1.
  • the experimental steel sample of the present disclosure exhibited very favorable hardness and toughness (CVN impact energy) relative to the conventional alloys. This was particularly unexpected and surprising.
  • Commercially available alloys providing comparable hardness and toughness typically are carbon steels, which would not withstand corrosive environments.
  • dual-phase stainless steels according to the present disclosure are prepared using conventional stainless steel production practices including, for example, melting of starting materials in an electric furnace, decarburization via AOD, and casting to an ingot.
  • Ingots may be cast, for example, by continuous casting or ingot pouring.
  • the cast material may be heat treated (austenitized) or sold as-rolled.
  • alloys according to the present disclosure are numerous. As described and evidenced above, the dual-phase stainless steels described herein are capable of being used in many applications where abrasion resistance and/or wear resistance is important. Articles of manufacture for which the steels according to the present disclosure would be particularly advantageous include, for example, parts and equipment used in oil sands extraction and parts and equipment used in sugar processing. Other applications for the stainless steels accoring to the present disclosure will be readily apprent to ordinarily skill practitioners. Those having ordinary skill may readily manufacture these and other articles of manufacture from the stainless steels according to the present disclosure using conventional manufacturing techniques.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
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US14/231,778 2014-04-01 2014-04-01 Dual-phase stainless steel Abandoned US20150275340A1 (en)

Priority Applications (15)

Application Number Priority Date Filing Date Title
US14/231,778 US20150275340A1 (en) 2014-04-01 2014-04-01 Dual-phase stainless steel
CN201580018031.2A CN106460128A (zh) 2014-04-01 2015-03-12 双相不锈钢
KR1020167028606A KR20160140733A (ko) 2014-04-01 2015-03-12 2상 스테인레스강
CA2944491A CA2944491A1 (en) 2014-04-01 2015-03-12 Dual-phase stainless steel
RU2016142683A RU2721668C2 (ru) 2014-04-01 2015-03-12 Двухфазная нержавеющая сталь
JP2016560351A JP6621419B2 (ja) 2014-04-01 2015-03-12 二相ステンレス鋼
MX2016012853A MX2016012853A (es) 2014-04-01 2015-03-12 Acero inoxidable de fase dual.
AU2015241412A AU2015241412B2 (en) 2014-04-01 2015-03-12 Dual-phase stainless steel
SI201531308T SI3126537T1 (sl) 2014-04-01 2015-03-12 Dvo-fazno nerjaveče jeklo
PL15712762T PL3126537T3 (pl) 2014-04-01 2015-03-12 Dwufazowa stal nierdzewna
PCT/US2015/020122 WO2015153092A1 (en) 2014-04-01 2015-03-12 Dual-phase stainless steel
EP15712762.2A EP3126537B1 (en) 2014-04-01 2015-03-12 Dual-phase stainless steel
ES15712762T ES2808627T3 (es) 2014-04-01 2015-03-12 Acero inoxidable de doble fase
TW104110764A TWI651419B (zh) 2014-04-01 2015-04-01 雙相不銹鋼
UAA201610885A UA119168C2 (uk) 2014-04-01 2015-12-03 Двофазна нержавіюча сталь

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US14/231,778 Abandoned US20150275340A1 (en) 2014-04-01 2014-04-01 Dual-phase stainless steel

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US (1) US20150275340A1 (ko)
EP (1) EP3126537B1 (ko)
JP (1) JP6621419B2 (ko)
KR (1) KR20160140733A (ko)
CN (1) CN106460128A (ko)
AU (1) AU2015241412B2 (ko)
CA (1) CA2944491A1 (ko)
ES (1) ES2808627T3 (ko)
MX (1) MX2016012853A (ko)
PL (1) PL3126537T3 (ko)
RU (1) RU2721668C2 (ko)
SI (1) SI3126537T1 (ko)
TW (1) TWI651419B (ko)
UA (1) UA119168C2 (ko)
WO (1) WO2015153092A1 (ko)

Cited By (4)

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Publication number Priority date Publication date Assignee Title
US10640854B2 (en) 2016-08-04 2020-05-05 Honda Motor Co., Ltd. Multi-material component and methods of making thereof
US11318566B2 (en) 2016-08-04 2022-05-03 Honda Motor Co., Ltd. Multi-material component and methods of making thereof
US11339817B2 (en) 2016-08-04 2022-05-24 Honda Motor Co., Ltd. Multi-material component and methods of making thereof
US11511375B2 (en) 2020-02-24 2022-11-29 Honda Motor Co., Ltd. Multi component solid solution high-entropy alloys

Citations (2)

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